diff --git a/.gitattributes b/.gitattributes index aa9ab32..1b9ff51 100644 --- a/.gitattributes +++ b/.gitattributes @@ -371,5 +371,6 @@ /Electrochemical/Cast_Stellite1_Sample1_Actual/OCP.cor filter=lfs diff=lfs merge=lfs -text /Electrochemical/Cast_Stellite1_Sample2_Actual/OCP.cor filter=lfs diff=lfs merge=lfs -text /Electrochemical/Cast_Stellite1_Sample3_Actual/OCP.cor filter=lfs diff=lfs merge=lfs -text +/Thesis.pdf filter=lfs diff=lfs merge=lfs -text *.jp*g filter=lfs diff=lfs merge=lfs -text *.tif filter=lfs diff=lfs merge=lfs -text diff --git a/Heriot_Watt_Thesis_Template.pdf b/Heriot_Watt_Thesis_Template.pdf deleted file mode 100644 index 8ff69f2..0000000 --- a/Heriot_Watt_Thesis_Template.pdf +++ /dev/null @@ -1,3 +0,0 @@ -version https://git-lfs.github.com/spec/v1 -oid sha256:aa02e87d04f46a26d2019cc690bfde459dd9a71c80ab367cd1e9362ec5a3d179 -size 428469 diff --git a/I-packages.tex b/I-packages.tex index b7f3a03..c6f86ad 100644 --- a/I-packages.tex +++ b/I-packages.tex @@ -6,7 +6,7 @@ \usepackage[T1]{fontenc} % font \usepackage{csquotes} %\usepackage[defernumbers=true, sorting=none]{biblatex} -\usepackage[defernumbers=true, sorting=none, style=authoryear, backend=biber, maxbibnames=999]{biblatex} +\usepackage[style=ieee, backend=biber, maxbibnames=999]{biblatex} \usepackage{setspace} % spacing % \usepackage[left=4cm,right=2cm,top=2cm,bottom=2cm]{geometry} diff --git a/Makefile b/Makefile new file mode 100644 index 0000000..e744016 --- /dev/null +++ b/Makefile @@ -0,0 +1,88 @@ +### latex.makefile +# Author: Jason Hiebel + +# This is a simple makefile for compiling LaTeX documents. The core assumption +# is that the resulting documents should have any parameters effecting +# rendering quality set to theoretical limits and that all fonts should be +# embedded. While typically overkill, the detriment to doing so is negligible. + +# Targets: +# default : compiles the document to a PDF file using the defined +# latex generating engine. (pdflatex, xelatex, etc) +# display : displays the compiled document in a common PDF viewer. +# (currently linux = evince, OSX = open) +# clean : removes the obj/ directory holding temporary files + +PROJECT = Thesis +default: obj/$(PROJECT).pdf + +display: default + (${PDFVIEWER} obj/$(PROJECT).pdf &) + + +### Compilation Flags +PDFLATEX_FLAGS = -halt-on-error -output-directory obj/ + +TEXINPUTS = .:obj/ +TEXMFOUTPUT = obj/ + + +### File Types (for dependancies) +TEX_FILES = $(shell find . -name '*.tex' -or -name '*.sty' -or -name '*.cls') +BIB_FILES = $(shell find . -name '*.bib') +BST_FILES = $(shell find . -name '*.bst') +IMG_FILES = $(shell find . -path '*.jpg' -or -path '*.png' -or \( \! -path './obj/*.pdf' -path '*.pdf' \) ) + + +### Standard PDF Viewers +# Defines a set of standard PDF viewer tools to use when displaying the result +# with the display target. Currently chosen are defaults which should work on +# most linux systems with GNOME installed and on all OSX systems. + +UNAME := $(shell uname) + +ifeq ($(UNAME), Linux) +PDFVIEWER = evince +endif + +#ifeq ($(UNAME), Darwin) +#PDFVIEWER = open +#endif + + +### Clean +# This target cleans the temporary files generated by the tex programs in +# use. All temporary files generated by this makefile will be placed in obj/ +# so cleanup is easy. + +clean:: + rm -rf obj/ + +### Core Latex Generation +# Performs the typical build process for latex generations so that all +# references are resolved correctly. If adding components to this run-time +# always take caution and implement the worst case set of commands. +# Example: latex, bibtex, latex, latex +# +# Note the use of order-only prerequisites (prerequisites following the |). +# Order-only prerequisites do not effect the target -- if the order-only +# prerequisite has changed and none of the normal prerequisites have changed +# then this target IS NOT run. +# +# In order to function for projects which use a subset of the provided features +# it is important to verify that optional dependancies exist before calling a +# target; for instance, see how bibliography files (.bbl) are handled as a +# dependency. + +obj/: + mkdir -p obj/ + +obj/$(PROJECT).aux: $(TEX_FILES) $(IMG_FILES) | obj/ + xelatex $(PDFLATEX_FLAGS) $(PROJECT) + +obj/$(PROJECT).bbl: $(BIB_FILES) | obj/$(PROJECT).aux + bibtex obj/$(PROJECT) + xelatex $(PDFLATEX_FLAGS) $(PROJECT) + +obj/$(PROJECT).pdf: obj/$(PROJECT).aux $(if $(BIB_FILES), obj/$(PROJECT).bbl) + xelatex $(PDFLATEX_FLAGS) $(PROJECT) diff --git a/Thesis.bbl b/Thesis.bbl new file mode 100644 index 0000000..4bcac41 --- /dev/null +++ b/Thesis.bbl @@ -0,0 +1,1568 @@ +% $ biblatex auxiliary file $ +% $ biblatex bbl format version 3.3 $ +% Do not modify the above lines! +% +% This is an auxiliary file used by the 'biblatex' package. +% This file may safely be deleted. It will be recreated by +% biber as required. +% +\begingroup +\makeatletter +\@ifundefined{ver@biblatex.sty} + {\@latex@error + {Missing 'biblatex' package} + {The bibliography requires the 'biblatex' package.} + \aftergroup\endinput} + {} +\endgroup + + +\refsection{0} + \datalist[entry]{none/global//global/global/global} + \entry{ahmedStructurePropertyRelationships2014}{article}{}{} + \name{author}{4}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=1c8f35a67217a8f6cbd1f8d3edb797b0}{% + family={Faisal}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi H.}, + giveni={N\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{fullhashraw}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{bibnamehash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authorbibnamehash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authorfullhashraw}{0ba22f8fbb626d88357e4651c3f66f4d} + \field{extraname}{1} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This investigation considered the multiscale tribo-mechanical evaluations of CoCrMo (Stellite®21) alloys manufactured via two different processing routes of casting and HIP-consolidation from powder (Hot Isostatic Pressing). These involved hardness, nanoscratch, impact toughness, abrasive wear and sliding wear evaluations using pin-on-disc and ball-on-flat tests. HIPing improved the nanoscratch and ball-on-flat sliding wear performance due to higher hardness and work-hardening rate of the metal matrix. The cast alloy however exhibited superior abrasive wear and self-mated pin-on-disc wear performance. The tribological properties were more strongly influenced by the CoCr matrix, which is demonstrated in nanoscratch analysis.} + \field{issn}{0301-679X} + \field{journaltitle}{Tribology International} + \field{month}{12} + \field{note}{24 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Structure–property relationships in a {CoCrMo} alloy at micro and nano-scales} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{80} + \field{year}{2014} + \field{urldateera}{ce} + \field{pages}{98\bibrangedash 114} + \range{pages}{17} + \verb{doi} + \verb 10.1016/j.triboint.2014.06.015 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X14002436 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X14002436 + \endverb + \keyw{Manufacturing,Nanoscratch,Nanotribology,Wear} + \endentry + \entry{malayogluComparingPerformanceHIPed2003}{article}{}{} + \name{author}{2}{}{% + {{hash=71f57eb10950396ed3fa62c703ddaee5}{% + family={Malayoglu}, + familyi={M\bibinitperiod}, + given={U.}, + giveni={U\bibinitperiod}}}% + {{hash=c00a172220606f67c3da2492047a9b71}{% + family={Neville}, + familyi={N\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{fullhash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{fullhashraw}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{bibnamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorbibnamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authornamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorfullhash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorfullhashraw}{49054a18ed24a57daa4c3278c94c6ce5} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In this paper, results from erosion–corrosion tests performed under liquid–solid erosion conditions in 3.5\% NaCl liquid medium are reported. The focus of the paper is to compare the behaviour of Cast and Hot Isostatically Pressed (HIPed) Stellite 6 alloy in terms of their electrochemical corrosion characteristics, their resistance to mechanical degradation and relationship between microstructure and degradation mechanisms. It has been shown that HIPed Stellite 6 possesses better erosion and erosion corrosion resistance than that of Cast Stellite 6 and two stainless steels (UNS S32760 and UNS S31603) under the same solid loading (200 and 500mg/l), and same temperature (20 and 50°C). The material removal mechanisms have been identified by using atomic force microscopy (AFM) and shown preferential removal of the Co-rich matrix to be less extensive on the HIPed material.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{8} + \field{note}{34 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{series}{14th {International} {Conference} on {Wear} of {Materials}} + \field{title}{Comparing the performance of {HIPed} and {Cast} {Stellite} 6 alloy in liquid–solid slurries} + \field{urlday}{17} + \field{urlmonth}{2} + \field{urlyear}{2025} + \field{volume}{255} + \field{year}{2003} + \field{urldateera}{ce} + \field{pages}{181\bibrangedash 194} + \range{pages}{14} + \verb{doi} + \verb 10.1016/S0043-1648(03)00287-4 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164803002874 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164803002874 + \endverb + \keyw{Cast Stellite 6,Corrosion,Erosion,HIPed,Liquid–solid slurries} + \endentry + \entry{davis2000nickel}{book}{}{} + \name{author}{2}{}{% + {{hash=d24975e937cc4c8eafeb981d8d16a1d4}{% + family={Davis}, + familyi={D\bibinitperiod}, + given={J.R.}, + giveni={J\bibinitperiod}}}% + {{hash=2e482fdb03378296689bc75a76c2bdc4}{% + family={Committee}, + familyi={C\bibinitperiod}, + given={A.S.M.I.H.}, + giveni={A\bibinitperiod}}}% + } + \list{publisher}{1}{% + {ASM International}% + } + \strng{namehash}{ded5e703628bfa51629c3e9340068998} + \strng{fullhash}{ded5e703628bfa51629c3e9340068998} + \strng{fullhashraw}{ded5e703628bfa51629c3e9340068998} + \strng{bibnamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authorbibnamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authornamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authorfullhash}{ded5e703628bfa51629c3e9340068998} + \strng{authorfullhashraw}{ded5e703628bfa51629c3e9340068998} + \field{sortinit}{3} + \field{sortinithash}{ad6fe7482ffbd7b9f99c9e8b5dccd3d7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{isbn}{978-0-87170-685-0} + \field{note}{tex.lccn: 00059348} + \field{series}{{ASM} specialty handbook} + \field{title}{Nickel, cobalt, and their alloys} + \field{year}{2000} + \verb{urlraw} + \verb https://books.google.ae/books?id=IePhmnbmRWkC + \endverb + \verb{url} + \verb https://books.google.ae/books?id=IePhmnbmRWkC + \endverb + \endentry + \entry{alimardaniEffectLocalizedDynamic2010}{article}{}{} + \name{author}{4}{}{% + {{hash=b1d020be51ce7b141b4cf03868da762c}{% + family={Alimardani}, + familyi={A\bibinitperiod}, + given={Masoud}, + giveni={M\bibinitperiod}}}% + {{hash=44e10f283ada211ed0a7aa6d9913d23f}{% + family={Fallah}, + familyi={F\bibinitperiod}, + given={Vahid}, + giveni={V\bibinitperiod}}}% + {{hash=5aaf85cb279ac1471a04ce9c932a1122}{% + family={Khajepour}, + familyi={K\bibinitperiod}, + given={Amir}, + giveni={A\bibinitperiod}}}% + {{hash=88451951b0b3c1cc4383d3cebfc151ac}{% + family={Toyserkani}, + familyi={T\bibinitperiod}, + given={Ehsan}, + giveni={E\bibinitperiod}}}% + } + \strng{namehash}{86846ed827567cfd839f7c014178ad64} + \strng{fullhash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{fullhashraw}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{bibnamehash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authorbibnamehash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authornamehash}{86846ed827567cfd839f7c014178ad64} + \strng{authorfullhash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authorfullhashraw}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In laser cladding, high cooling rates create outcomes with superior mechanical and metallurgical properties. However, this characteristic along with the additive nature of the process significantly contributes to the formation of thermal stresses which are the main cause of any potential delamination and crack formation across the deposited layers. This drawback is more prominent for additive materials such as Stellite 1 which are by nature crack-sensitive during the hardfacing process. In this work, parallel to the experimental investigation, a numerical model is used to study the temperature distributions and thermal stresses throughout the deposition of Stellite 1 for hardfacing application. To manage the thermal stresses, the effect of preheating the substrate in a localized dynamic fashion is investigated. The numerical and experimental analyses are conducted by the deposition of Stellite 1 powder on the substrate of AISI-SAE 4340 alloy steel using a 1.1kW fiber laser. Experimental results confirm that by preheating the substrate a crack-free coating layer of Stellite 1 well-bonded to the substrate with a uniform dendritic structure, well-distributed throughout the deposited layer, can be obtained contrary to non-uniform structures formed in the coating of the non-preheated substrate with several cracks.} + \field{issn}{0257-8972} + \field{journaltitle}{Surface and Coatings Technology} + \field{month}{8} + \field{note}{64 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{23} + \field{title}{The effect of localized dynamic surface preheating in laser cladding of {Stellite} 1} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{204} + \field{year}{2010} + \field{urldateera}{ce} + \field{pages}{3911\bibrangedash 3919} + \range{pages}{9} + \verb{doi} + \verb 10.1016/j.surfcoat.2010.05.009 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0257897210003701 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0257897210003701 + \endverb + \keyw{Crack formation,Hardfacing alloys,Laser cladding,Preheating process,Temperature and thermal stress fields} + \endentry + \entry{ahmedMappingMechanicalProperties2023}{article}{}{} + \name{author}{3}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=8da5f61983121a25e044ca92bd036b2a}{% + family={Fardan}, + familyi={F\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{fullhashraw}{b3a15b2b31620e3640b3b3a16271687c} + \strng{bibnamehash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authorbibnamehash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authorfullhashraw}{b3a15b2b31620e3640b3b3a16271687c} + \field{extraname}{2} + \field{sortinit}{6} + \field{sortinithash}{b33bc299efb3c36abec520a4c896a66d} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Stellite alloys have good wear resistance and maintain their strength up to 600°C, making them suitable for various industrial applications like cutting tools and combustion engine parts. This investigation was aimed at i) manufacturing new Stellite alloy blends using powder metallurgy and ii) mathematically mapping hardness, yield strength, ductility and impact energy of base and alloy blends. Linear, exponential, polynomial approximations and dimensional analyses were conducted in this semi-empirical mathematical modelling approach. Base alloy compositions similar to Stellite 1, 4, 6, 12, 20 and 190 were used in this investigation to form new alloys via blends. The microstructure was analysed using Scanning Electron Microscopy (SEM) and X-ray Diffraction (XRD). Mechanical performance of alloys was conducted using tensile, hardness and Charpy impact tests. MATLAB® coding was used for the development of property maps. This investigation indicates that hardness and yield strength can be linked to the wt.\% composition of carbon and tungsten using linear approximation with a maximum variance of 5\% and 20\%, respectively. Elongation and carbide fraction showed a non-linear relationship with alloy composition. Impact energy was linked with elongation through polynomial approximation. A dimensional analysis was developed by interlinking carbide fraction, hardness, yield strength, and elongation to impact energy.} + \field{issn}{2374-068X} + \field{journaltitle}{Advances in Materials and Processing Technologies} + \field{month}{6} + \field{note}{1 citations (Semantic Scholar/DOI) [2025-04-12] Publisher: Taylor \& Francis \_eprint: https://doi.org/10.1080/2374068X.2023.2220242} + \field{number}{0} + \field{title}{Mapping the mechanical properties of cobalt-based stellite alloys manufactured via blending} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{0} + \field{year}{2023} + \field{urldateera}{ce} + \field{pages}{1\bibrangedash 30} + \range{pages}{30} + \verb{doi} + \verb 10.1080/2374068X.2023.2220242 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1080/2374068X.2023.2220242 + \endverb + \verb{url} + \verb https://doi.org/10.1080/2374068X.2023.2220242 + \endverb + \keyw{Blending,Hiping,Mathematical model,Powder metallurgy,Stellite alloys,Structure-property relationships} + \endentry + \entry{bunchCorrosionGallingResistant1989}{inproceedings}{}{} + \name{author}{3}{}{% + {{hash=ff8de9c468efb7eab8b92e573d3949ed}{% + family={Bunch}, + familyi={B\bibinitperiod}, + given={P.\bibnamedelimi O.}, + giveni={P\bibinitperiod\bibinitdelim O\bibinitperiod}}}% + {{hash=47f88033d1313a3ac56378baefb344e4}{% + family={Hartmann}, + familyi={H\bibinitperiod}, + given={M.\bibnamedelimi P.}, + giveni={M\bibinitperiod\bibinitdelim P\bibinitperiod}}}% + {{hash=7f4198582fc42b8ddab60cd433790594}{% + family={Bednarowicz}, + familyi={B\bibinitperiod}, + given={T.\bibnamedelimi A.}, + giveni={T\bibinitperiod\bibinitdelim A\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \list{publisher}{1}{% + {OnePetro}% + } + \strng{namehash}{b4088224b2a9ea87c42c7ab641ebe2de} + \strng{fullhash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{fullhashraw}{27ba512d074ac1ae4276e7a91ea23549} + \strng{bibnamehash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authorbibnamehash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authornamehash}{b4088224b2a9ea87c42c7ab641ebe2de} + \strng{authorfullhash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authorfullhashraw}{27ba512d074ac1ae4276e7a91ea23549} + \field{sortinit}{7} + \field{sortinithash}{108d0be1b1bee9773a1173443802c0a3} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{ABSTRACT. Application of corrosion resistant hardfacing materials are required to maintain exceptional reliability for metal to metal sealing in high pressure gate valves used for offshore production wells. New hardfacing materials have been developed and tailored for use where defense against degradation effects of high temperature, high pressure, H2S, C02, free sulfur and brine environments is required. Using a plasma transferred arc (PTA) weld process, new hardfacings of Stellite cobalt base materials have been successfully applied to nickel base alloy substrates. These hardfacings provide exceptional corrosion resistance over previously used materials produced by spray and fuse as well as high velocity combustion spray (} + \field{month}{5} + \field{note}{1 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Corrosion/{Galling} {Resistant} {Hardfacing} {Materials} for {Offshore} {Production} {Valves}} + \field{urlday}{1} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{year}{1989} + \field{urldateera}{ce} + \verb{doi} + \verb 10.4043/6070-MS + \endverb + \verb{urlraw} + \verb https://dx.doi.org/10.4043/6070-MS + \endverb + \verb{url} + \verb https://dx.doi.org/10.4043/6070-MS + \endverb + \endentry + \entry{ratiaComparisonSlidingWear2019}{article}{}{} + \name{author}{7}{}{% + {{hash=4d8d77bd60a2e1fd293e809631bc5a84}{% + family={Ratia}, + familyi={R\bibinitperiod}, + given={Vilma\bibnamedelima L.}, + giveni={V\bibinitperiod\bibinitdelim L\bibinitperiod}}}% + {{hash=84a91dba5410e2e8f67915c4c17aea08}{% + family={Zhang}, + familyi={Z\bibinitperiod}, + given={Deen}, + giveni={D\bibinitperiod}}}% + {{hash=f9e5a7fad20d40241ed0f25f05849207}{% + family={Carrington}, + familyi={C\bibinitperiod}, + given={Matthew\bibnamedelima J.}, + giveni={M\bibinitperiod\bibinitdelim J\bibinitperiod}}}% + {{hash=a61a195bd0ed9f39c9d446f02d7b9592}{% + family={Daure}, + familyi={D\bibinitperiod}, + given={Jaimie\bibnamedelima L.}, + giveni={J\bibinitperiod\bibinitdelim L\bibinitperiod}}}% + {{hash=d9e3c0caaa2d6903c488a2973cea1fd8}{% + family={McCartney}, + familyi={M\bibinitperiod}, + given={D.\bibnamedelimi Graham}, + giveni={D\bibinitperiod\bibinitdelim G\bibinitperiod}}}% + {{hash=d69de7eb40c8f8c0c78825838cd1f8ee}{% + family={Shipway}, + familyi={S\bibinitperiod}, + given={Philip\bibnamedelima H.}, + giveni={P\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=b150a22a65dc3516b89a2bd86a0e25ff}{% + family={Stewart}, + familyi={S\bibinitperiod}, + given={David\bibnamedelima A.}, + giveni={D\bibinitperiod\bibinitdelim A\bibinitperiod}}}% + } + \strng{namehash}{0f5fdf8e51bf5515e4025351773003d8} + \strng{fullhash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{fullhashraw}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{bibnamehash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authorbibnamehash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authornamehash}{0f5fdf8e51bf5515e4025351773003d8} + \strng{authorfullhash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authorfullhashraw}{2e0376be46be3b8d245d5ab5620f4ca2} + \field{sortinit}{8} + \field{sortinithash}{a231b008ebf0ecbe0b4d96dcc159445f} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Cobalt-based alloys such as Stellite 3 and Stellite 6 are widely used to protect stainless steel surfaces in primary circuit nuclear reactor applications where high resistance to wear and corrosion are required. In this study, self-mated sliding wear of Stellite 3 and Stellite 6 consolidated by hot isostatic pressing were compared. Tests were performed with a pin-on-disc apparatus enclosed in a water-submerged autoclave environment and wear was measured from room temperature up to 250 °C (a representative pressurized water reactor environment). Both alloys exhibit a microstructure of micron-sized carbides embedded in a cobalt-rich matrix. Stellite 3 (higher tungsten and carbon content) contains M7C3 and an eta (η) -carbide whereas Stellite 6 contains only M7C3. Furthermore, the former has a significantly higher carbide volume fraction and hardness than the latter. Both alloys show a significant increase in the wear rate as the temperature is increased but Stellite 3 has a higher wear resistance over the entire range; at 250 °C the wear rate of Stellite 6 is more than five times that of Stellite 3. There is only a minimal formation of a transfer layer on the sliding surfaces but electron backscatter diffraction on cross-sections through the wear scar revealed that wear causes partial transformation of the cobalt matrix from fcc to hcp in both alloys over the entire temperature range. It is proposed that the acceleration of wear with increasing temperature in the range studied is associated with a tribocorrosion mechanism and that the higher carbide fraction in Stellite 3 resulted in its reduced wear rate compared to Stellite 6.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{4} + \field{note}{20 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{series}{22nd {International} {Conference} on {Wear} of {Materials}} + \field{title}{Comparison of the sliding wear behaviour of self-mated {HIPed} {Stellite} 3 and {Stellite} 6 in a simulated {PWR} water environment} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{426-427} + \field{year}{2019} + \field{urldateera}{ce} + \field{pages}{1222\bibrangedash 1232} + \range{pages}{11} + \verb{doi} + \verb 10.1016/j.wear.2019.01.116 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S004316481930211X + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S004316481930211X + \endverb + \keyw{Cobalt-based alloys,Electron backscatter diffraction,HIP,Nuclear,Stellite} + \endentry + \entry{zhangFrictionWearCharacterization2002}{article}{}{} + \name{author}{2}{}{% + {{hash=9ac5c6e1891a9d327b6cf9dce9924eaa}{% + family={Zhang}, + familyi={Z\bibinitperiod}, + given={K}, + giveni={K\bibinitperiod}}}% + {{hash=cb8741204d7e12b6db11ee35f025c97c}{% + family={Battiston}, + familyi={B\bibinitperiod}, + given={L}, + giveni={L\bibinitperiod}}}% + } + \strng{namehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{fullhash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{fullhashraw}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{bibnamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorbibnamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authornamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorfullhash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorfullhashraw}{bf171f4e97c3179e4c0d9908cf319a1f} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{A full-journal submerged bearing test rig was built to evaluate the friction and wear behavior of materials in zinc alloy baths. Some cobalt- and iron-based superalloys were tested using this rig at conditions similar to those of a continuous galvanizing operation (load and bath chemistry). Metallographic and chemical analyses were conducted on tested samples to characterize the wear. It was found that a commonly used cobalt-based material (Stellite \#6) not only suffered considerable wear but also reacted with zinc baths to form intermetallic compounds. Other cobalt- and iron-based superalloys appeared to have negligible reaction with the zinc baths in the short-term tests, but cracks developed in the sub-surface, suggesting that the materials mainly experienced surface fatigue wear. The commonly used cobalt-based superalloy mostly experienced abrasive wear.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{33 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{3} + \field{title}{Friction and wear characterization of some cobalt- and iron-based superalloys in zinc alloy baths} + \field{urlday}{1} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{252} + \field{year}{2002} + \field{urldateera}{ce} + \field{pages}{332\bibrangedash 344} + \range{pages}{13} + \verb{doi} + \verb 10.1016/S0043-1648(01)00889-4 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164801008894 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164801008894 + \endverb + \keyw{Friction and wear,Galvanizing,Submerged hardware,Superalloys} + \endentry + \entry{ashworthMicrostructurePropertyRelationships1999}{article}{}{} + \name{author}{3}{}{% + {{hash=a0a9668f5a93080c8425a8cf80e9d0d2}{% + family={Ashworth}, + familyi={A\bibinitperiod}, + given={M.A.}, + giveni={M\bibinitperiod}}}% + {{hash=27753a82b6390957cb920ec5052f0810}{% + family={Jacobs}, + familyi={J\bibinitperiod}, + given={M.H.}, + giveni={M\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \list{language}{1}{% + {EN}% + } + \strng{namehash}{abac9b3a3bd887c0c8dedb4a4e169c92} + \strng{fullhash}{68dce5901af799f73fc399cf947f81b9} + \strng{fullhashraw}{68dce5901af799f73fc399cf947f81b9} + \strng{bibnamehash}{68dce5901af799f73fc399cf947f81b9} + \strng{authorbibnamehash}{68dce5901af799f73fc399cf947f81b9} + \strng{authornamehash}{abac9b3a3bd887c0c8dedb4a4e169c92} + \strng{authorfullhash}{68dce5901af799f73fc399cf947f81b9} + \strng{authorfullhashraw}{68dce5901af799f73fc399cf947f81b9} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In the present paper the microstructure and properties of a range of hipped Stellite powders are investigated, the basic aim of the study being to generate a materia/property database to facilitate alloy selection for potential applications involving net shape component manufacture. Particular attention is paid to the morphology, particle size distribution, and surface composition of the as atomised powders and their effect on subsequent consolidation. The consolidated powders are fully characterised in terms of microstructure and the composition and distribution of secondary phases. The effect of hipping temperature on the microstructure, hardness, and tensile properties of the powders are discussed in terms of the optimum processing temperature for the various alloys.} + \field{issn}{0032-5899} + \field{journaltitle}{Powder Metallurgy} + \field{month}{3} + \field{note}{23 citations (Semantic Scholar/DOI) [2025-04-12] Publisher: SAGE Publications} + \field{number}{3} + \field{title}{Microstructure and property relationships in hipped {Stellite} powders} + \field{urlday}{3} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{42} + \field{year}{1999} + \field{urldateera}{ce} + \field{pages}{243\bibrangedash 249} + \range{pages}{7} + \verb{doi} + \verb 10.1179/003258999665585 + \endverb + \verb{urlraw} + \verb https://journals.sagepub.com/action/showAbstract + \endverb + \verb{url} + \verb https://journals.sagepub.com/action/showAbstract + \endverb + \endentry + \entry{ferozhkhanMetallurgicalStudyStellite2017}{article}{}{} + \name{author}{3}{}{% + {{hash=bed071d3745587c303d1b4411281a295}{% + family={Ferozhkhan}, + familyi={F\bibinitperiod}, + given={Mohammed\bibnamedelima Mohaideen}, + giveni={M\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=fdb6a42317e0e10a267ce7c918a63e11}{% + family={Kumar}, + familyi={K\bibinitperiod}, + given={Kottaimathan\bibnamedelima Ganesh}, + giveni={K\bibinitperiod\bibinitdelim G\bibinitperiod}}}% + {{hash=250edfbd96cbc7ebd974dd11a2098198}{% + family={Ravibharath}, + familyi={R\bibinitperiod}, + given={Rajanbabu}, + giveni={R\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \strng{namehash}{7a694c7ba4c57888494ddc3675c7d70c} + \strng{fullhash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{fullhashraw}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{bibnamehash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authorbibnamehash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authornamehash}{7a694c7ba4c57888494ddc3675c7d70c} + \strng{authorfullhash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authorfullhashraw}{c63a5ee4b2edf1e71712795226de5b1a} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{309-16L stainless steel was deposited over base metal Grade 91 steel (9Cr–1Mo) as buffer layer by shielded metal arc welding (SMAW), gas tungsten arc welding (GTAW) and flux cored arc welding processes, and then, Stellite 6 (Co–Cr alloy) was coated on stainless steel buffer by SMAW, GTAW and plasma transferred arc welding processes. Stellite 6 coatings were characterized using optical microscope, Vickers hardness tester and optical emission spectrometer, respectively. The FCA deposit has less heat-affected zone and uniform hardness than SMA and GTA deposits. The buffer layer has reduced the formation of any surface cracks and delamination near the fusion zones. The microstructure of Stellite 6 consists of dendrites of Co solid solution and carbides secretion in the interdendrites of Co and Cr matrix. Electron-dispersive spectroscopy line scan has been conducted to analyse the impact of alloying elements in the fusion line and Stellite 6 deposits. It was observed that dilution of Fe in PTA-deposited Stellite 6 was lesser than SMA and GTA deposits and uniform hardness of 600–650 \$\${\textbackslash}hbox \{HV\}\_\{0.3\}\$\$was obtained from PTA deposit. The chemical analysis resulted in alloy composition of PTA deposit has nominal percentage in comparison with consumable composition while GTA and SMA deposits has high dilution of Fe and Ni.} + \field{issn}{2191-4281} + \field{journaltitle}{Arabian Journal for Science and Engineering} + \field{month}{5} + \field{note}{0 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{5} + \field{title}{Metallurgical {Study} of {Stellite} 6 {Cladding} on 309-{16L} {Stainless} {Steel}} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{42} + \field{year}{2017} + \field{urldateera}{ce} + \field{pages}{2067\bibrangedash 2074} + \range{pages}{8} + \verb{doi} + \verb 10.1007/s13369-017-2457-7 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/s13369-017-2457-7 + \endverb + \verb{url} + \verb https://doi.org/10.1007/s13369-017-2457-7 + \endverb + \keyw{Dilution,EDS,Hardfacing,Interdendrites,Stellite} + \endentry + \entry{pacquentinTemperatureInfluenceRepair2025}{article}{}{} + \name{author}{5}{}{% + {{hash=096b7ba62dd31bb3abb4c7daa2ba6477}{% + family={Pacquentin}, + familyi={P\bibinitperiod}, + given={Wilfried}, + giveni={W\bibinitperiod}}}% + {{hash=9e420ee86aa957c365d57085e999996c}{% + family={Wident}, + familyi={W\bibinitperiod}, + given={Pierre}, + giveni={P\bibinitperiod}}}% + {{hash=268ededdba463184d10a8f5532d5cf81}{% + family={Varlet}, + familyi={V\bibinitperiod}, + given={Jérôme}, + giveni={J\bibinitperiod}}}% + {{hash=b24f3669f2a577f8062abf9d04e0e179}{% + family={Cailloux}, + familyi={C\bibinitperiod}, + given={Thomas}, + giveni={T\bibinitperiod}}}% + {{hash=ba3f789128096170532622dc53c3bbd0}{% + family={Maskrot}, + familyi={M\bibinitperiod}, + given={Hicham}, + giveni={H\bibinitperiod}}}% + } + \strng{namehash}{f57606f1b71f32267dc7727ee385b008} + \strng{fullhash}{0cc41d1605707534d43f79ae97691cbc} + \strng{fullhashraw}{0cc41d1605707534d43f79ae97691cbc} + \strng{bibnamehash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authorbibnamehash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authornamehash}{f57606f1b71f32267dc7727ee385b008} + \strng{authorfullhash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authorfullhashraw}{0cc41d1605707534d43f79ae97691cbc} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Additive manufacturing (AM) is a proven time- and cost-effective method for repairing parts locally damaged after e.g. repetitive friction wear or corrosion. Repairing a hardfacing coating using AM technologies presents however several simultaneous challenges arising from the complex geometry and a high probability of crack formation due to process-induced stress. We address the repair of a cobalt-based Stellite™ 6 hardfacing coating on an AISI 316L substrate performed using Laser Powder Directed Energy Deposition (LP-DED) and investigate the influence of key process features and parameters. We describe our process which successfully prevents crack formation both during and after the repair, highlighting the design of the preliminary part machining phase, induction heating of an extended part volume during the laser repair phase and the optimal scanning strategy. Local characterization using non-destructive testing, Vickers hardness measurements and microstructural examinations by scanning electron microscopy (SEM) show an excellent metallurgical quality of the repair and its interface with the original part. In addition, we introduce an innovative process qualification test assessing the repair quality and innocuity, which is based on the global response to induced cracks and probes the absence of crack attraction by the repair (ACAR11ACAR stands for absence of crack attraction by the repair.). Here this ACAR test reveals a slight difference in mechanical behavior between the repair and the original coating which motivates further work to eventually make the repair imperceptible.} + \field{issn}{2666-3309} + \field{journaltitle}{Journal of Advanced Joining Processes} + \field{month}{6} + \field{title}{Temperature influence on the repair of a hardfacing coating using laser metal deposition and assessment of the repair innocuity} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{11} + \field{year}{2025} + \field{urldateera}{ce} + \field{pages}{100284} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.jajp.2025.100284 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S2666330925000056 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S2666330925000056 + \endverb + \keyw{Additive manufacturing,Direct laser deposition,Hardfacing coating,Mechanical characterization,Repair,Repair innocuity assessment} + \endentry + \entry{desaiEffectCarbideSize1984}{article}{}{} + \name{author}{4}{}{% + {{hash=fc05df304d9bc11398a5c124af37591d}{% + family={Desai}, + familyi={D\bibinitperiod}, + given={V.\bibnamedelimi M.}, + giveni={V\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=ec550afc1e3aea4900fb58655a64f6da}{% + family={Rao}, + familyi={R\bibinitperiod}, + given={C.\bibnamedelimi M.}, + giveni={C\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=33b6be2f67c7c521e0d9dd2e94cb03fa}{% + family={Kosel}, + familyi={K\bibinitperiod}, + given={T.\bibnamedelimi H.}, + giveni={T\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=1ad7f5a75d8dc26e538ca7e4d233e622}{% + family={Fiore}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi F.}, + giveni={N\bibinitperiod\bibinitdelim F\bibinitperiod}}}% + } + \strng{namehash}{aeae2b334e415789011cf05b2beda57d} + \strng{fullhash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{fullhashraw}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{bibnamehash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authorbibnamehash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authornamehash}{aeae2b334e415789011cf05b2beda57d} + \strng{authorfullhash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authorfullhashraw}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{A study of the effect of carbide size on the abrasion resistance of two cobalt-base powder metallurgy alloys, alloys 6 and 19, was conducted using low stress abrasion with a relatively hard abrasive, A12O3. Specimens of each alloy were produced with different carbide sizes but with a constant carbide volume fraction. The wear test results show a monotonie decrease in wear rate with increasing carbide size. Scanning electron microscopy of the worn surfaces and of wear debris particles shows that the primary material removal mechanism is micromachining. Small carbides provide little resistance to micromachining because of the fact that many of them are contained entirely in the volume of micromachining chips. The large carbides must be directly cut by the abrasive particles. Other less frequently observed material removal mechanisms included direct carbide pull-out and the formation of large pits in fine carbide specimens. These processes are considered secondary in the present work, but they may have greater importance in wear by relatively soft abrasives which do not cut chips from the carbide phase of these alloys. Some indication of this is provided by limited studies using a relatively soft abrasive, rounded quartz.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{59 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{title}{Effect of carbide size on the abrasion of cobalt-base powder metallurgy alloys} + \field{urlday}{17} + \field{urlmonth}{11} + \field{urlyear}{2024} + \field{volume}{94} + \field{year}{1984} + \field{urldateera}{ce} + \field{pages}{89\bibrangedash 101} + \range{pages}{13} + \verb{doi} + \verb 10.1016/0043-1648(84)90168-6 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/0043164884901686 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/0043164884901686 + \endverb + \keyw{Cavitation,Cavitation equipment,Damage measurement,Instrumentation,Sodium} + \endentry + \entry{francCavitationErosion2005}{incollection}{}{} + \name{editor}{2}{}{% + {{hash=82466166f53e07ad9568dba9555563e7}{% + family={Franc}, + familyi={F\bibinitperiod}, + given={Jean-Pierre}, + giveni={J\bibinithyphendelim P\bibinitperiod}}}% + {{hash=441eced1863753c712f0eaa788cbc3d5}{% + family={Michel}, + familyi={M\bibinitperiod}, + given={Jean-Marie}, + giveni={J\bibinithyphendelim M\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \list{location}{1}{% + {Dordrecht}% + } + \list{publisher}{1}{% + {Springer Netherlands}% + } + \strng{namehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{fullhash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{fullhashraw}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{bibnamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorbibnamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editornamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorfullhash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorfullhashraw}{9ef3cd89643a1a5e288c68eb93b9390c} + \field{sortinit}{4} + \field{sortinithash}{9381316451d1b9788675a07e972a12a7} + \field{labelnamesource}{editor} + \field{labeltitlesource}{title} + \field{booktitle}{Fundamentals of {Cavitation}} + \field{isbn}{978-1-4020-2233-3} + \field{title}{Cavitation {Erosion}} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{year}{2005} + \field{urldateera}{ce} + \field{pages}{265\bibrangedash 291} + \range{pages}{27} + \verb{doi} + \verb 10.1007/1-4020-2233-6_12 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/1-4020-2233-6_12 + \endverb + \verb{url} + \verb https://doi.org/10.1007/1-4020-2233-6_12 + \endverb + \keyw{Acoustic Impedance,Adverse Pressure Gradient,Mass Loss Rate,Pressure Pulse,Solid Wall} + \endentry + \entry{romoCavitationHighvelocitySlurry2012}{article}{}{} + \name{author}{4}{}{% + {{hash=abd07783347fdc165942b01479e16afb}{% + family={Romo}, + familyi={R\bibinitperiod}, + given={S.A.}, + giveni={S\bibinitperiod}}}% + {{hash=9c9837ed5fce5c7a1aeb233aa99aa04d}{% + family={Santa}, + familyi={S\bibinitperiod}, + given={J.F.}, + giveni={J\bibinitperiod}}}% + {{hash=fecaae68172b53756247ca68af700ed9}{% + family={Giraldo}, + familyi={G\bibinitperiod}, + given={J.E.}, + giveni={J\bibinitperiod}}}% + {{hash=467faf266d1206e4566fe6d0465b33f0}{% + family={Toro}, + familyi={T\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{285bcf9d2b83436d537b5e21b7fde046} + \strng{fullhash}{e0312588d226589c879f5d182ca350e9} + \strng{fullhashraw}{e0312588d226589c879f5d182ca350e9} + \strng{bibnamehash}{e0312588d226589c879f5d182ca350e9} + \strng{authorbibnamehash}{e0312588d226589c879f5d182ca350e9} + \strng{authornamehash}{285bcf9d2b83436d537b5e21b7fde046} + \strng{authorfullhash}{e0312588d226589c879f5d182ca350e9} + \strng{authorfullhashraw}{e0312588d226589c879f5d182ca350e9} + \field{sortinit}{4} + \field{sortinithash}{9381316451d1b9788675a07e972a12a7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The cavitation and slurry erosion resistances of Stellite 6 coatings and 13-4 stainless steel were compared in laboratory. The Cavitation Resistance (CR) was measured according to ASTM G32 standard and the Slurry Erosion Resistance (SER) was tested in a high-velocity erosion tester under several impact angles. The results showed that the coatings improved the CR 15 times when compared to bare stainless steel. The SER of the coatings was also higher for all the impingement angles tested, the highest erosion rate being observed at 45°. The main wear mechanisms were micro-cracking (cavitation tests), and micro-cutting and micro-ploughing (slurry erosion tests). © 2011 Elsevier Ltd. All rights reserved.} + \field{issn}{0301679X (ISSN)} + \field{journaltitle}{Tribology International} + \field{note}{82 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Cavitation and high-velocity slurry erosion resistance of welded {Stellite} 6 alloy} + \field{volume}{47} + \field{year}{2012} + \field{pages}{16\bibrangedash 24} + \range{pages}{9} + \verb{doi} + \verb 10.1016/j.triboint.2011.10.003 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-84856240362&doi=10.1016%2fj.triboint.2011.10.003&partnerID=40&md5=77bc5b529937543083c683cc6f5d689d + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-84856240362&doi=10.1016%2fj.triboint.2011.10.003&partnerID=40&md5=77bc5b529937543083c683cc6f5d689d + \endverb + \keyw{Cavitation,Cavitation corrosion,Cavitation erosion,Cavitation resistance,Cerium alloys,Chromate coatings,Erosion,Erosion rates,High velocity,Impact angles,Impact resistance,Impingement angle,Micro-cutting,Slurry erosion,Stainless steel,Stellite,Stellite 6,Stellite 6 alloy,Stellite 6 coating,Tribology,Wear mechanisms,alloy} + \endentry + \entry{gevariDirectIndirectThermal2020}{article}{}{} + \name{author}{5}{}{% + {{hash=93d9cff817608f96c206941face4c5d7}{% + family={Gevari}, + familyi={G\bibinitperiod}, + given={Moein\bibnamedelima Talebian}, + giveni={M\bibinitperiod\bibinitdelim T\bibinitperiod}}}% + {{hash=e271948379fd6fee4bd30a4d576761b8}{% + family={Abbasiasl}, + familyi={A\bibinitperiod}, + given={Taher}, + giveni={T\bibinitperiod}}}% + {{hash=67d0558f57dbf7548b5b43a80b85f47f}{% + family={Niazi}, + familyi={N\bibinitperiod}, + given={Soroush}, + giveni={S\bibinitperiod}}}% + {{hash=efb87c095e41c6349ba97d939982e130}{% + family={Ghorbani}, + familyi={G\bibinitperiod}, + given={Morteza}, + giveni={M\bibinitperiod}}}% + {{hash=311cf929c32c6c2ce5aa2728ae09ad47}{% + family={Koşar}, + familyi={K\bibinitperiod}, + given={Ali}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{76843143b68c90c6ac5d9d854fd56c1f} + \strng{fullhash}{7e654139b427bf36f3a25a5848105f5b} + \strng{fullhashraw}{7e654139b427bf36f3a25a5848105f5b} + \strng{bibnamehash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authorbibnamehash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authornamehash}{76843143b68c90c6ac5d9d854fd56c1f} + \strng{authorfullhash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authorfullhashraw}{7e654139b427bf36f3a25a5848105f5b} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{shorttitle} + \field{abstract}{The phase change phenomenon in fluids as a result of low local pressure under a critical value is known as cavitation. Acoustic wave propagation or hydrodynamic pressure drop of the working fluid are the main reasons for inception of this phenomenon. Considering the released energy from the collapsing cavitation bubbles as a reliable source has led to its implementation to different fields, namely, heat transfer, surface cleaning and fouling, water treatment, food industry, chemical reactions, energy harvesting. A considerable amount of energy in the mentioned industries is required for thermal applications. Cavitation could serve for minimizing the energy demand and optimizing the processes. Thus, the energy efficiency of the systems could be significantly enhanced. This review article focuses on the direct and indirect thermal applications of hydrodynamic and acoustic cavitation. Relevant studies with emerging applications are discussed, while developments in cavitation, which have given rise to thermal applications during the last decade, are also included in this review.} + \field{issn}{1359-4311} + \field{journaltitle}{Applied Thermal Engineering} + \field{month}{5} + \field{note}{84 citations (Semantic Scholar/DOI) [2025-04-13]} + \field{shorttitle}{Direct and indirect thermal applications of hydrodynamic and acoustic cavitation} + \field{title}{Direct and indirect thermal applications of hydrodynamic and acoustic cavitation: {A} review} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{171} + \field{year}{2020} + \field{urldateera}{ce} + \field{pages}{115065} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.applthermaleng.2020.115065 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S135943111937766X + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S135943111937766X + \endverb + \keyw{Acoustic cavitation,Food industry,Heat transfer enhancement,Hydrodynamic cavitation,Water treatment} + \endentry + \entry{shinEffectMolybdenumMicrostructure2003}{article}{}{} + \name{author}{5}{}{% + {{hash=11c1c63fde4778e27fd93d2389dd1d9f}{% + family={Shin}, + familyi={S\bibinitperiod}, + given={Jong-Choul}, + giveni={J\bibinithyphendelim C\bibinitperiod}}}% + {{hash=4d7d3c5a5d25916fcbdacaec6e7b281c}{% + family={Doh}, + familyi={D\bibinitperiod}, + given={Jung-Man}, + giveni={J\bibinithyphendelim M\bibinitperiod}}}% + {{hash=9257782113324f27de8d34043cd84f7b}{% + family={Yoon}, + familyi={Y\bibinitperiod}, + given={Jin-Kook}, + giveni={J\bibinithyphendelim K\bibinitperiod}}}% + {{hash=f1733c8d49f956fedeb6a8c03ce455c9}{% + family={Lee}, + familyi={L\bibinitperiod}, + given={Dok-Yol}, + giveni={D\bibinithyphendelim Y\bibinitperiod}}}% + {{hash=d2534382552f3c10ee00cd39f0979de1}{% + family={Kim}, + familyi={K\bibinitperiod}, + given={Jae-Soo}, + giveni={J\bibinithyphendelim S\bibinitperiod}}}% + } + \strng{namehash}{35defe2b8f7d338cdec33698baeff00a} + \strng{fullhash}{178cbc46d086767ebf3c6301cad009cf} + \strng{fullhashraw}{178cbc46d086767ebf3c6301cad009cf} + \strng{bibnamehash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authorbibnamehash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authornamehash}{35defe2b8f7d338cdec33698baeff00a} + \strng{authorfullhash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authorfullhashraw}{178cbc46d086767ebf3c6301cad009cf} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The Stellite 6 hardfacing alloys with different Mo contents have been deposited on AISI 1045-carbon steel using a Plasma Transferred Arc (PTA) welding machine. The effect of Mo on the microstructures and wear resistance properties of the Stellite 6 hardfacing alloys were investigated using optical microscopy, scanning electron microscopy, electron probe microanalysis and X-ray diffraction. With an increase in Mo contents, the M23C6 and M6C type carbides were formed instead of Cr-rich M7C3 and M23C6 type carbides observed in the interdenritic region of the Mo-free Stellite 6 hardfacing alloy. The size of Cr-rich carbides in interdendritic region decreased, but that of M6C type carbide increased as well as the refinement of Co-rich dendrites. The volume fraction of Cr-rich carbides slightly increased, but that of M6C type carbide abruptly increased. This microstructural change was responsible for the improvement of the mechanical properties such as hardness and wear resistance of the Mo-modified Stellite 6 hardfacing alloy.} + \field{issn}{0257-8972} + \field{journaltitle}{Surface and Coatings Technology} + \field{month}{3} + \field{number}{2} + \field{title}{Effect of molybdenum on the microstructure and wear resistance of cobalt-base {Stellite} hardfacing alloys} + \field{urlday}{5} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{166} + \field{year}{2003} + \field{urldateera}{ce} + \field{pages}{117\bibrangedash 126} + \range{pages}{10} + \verb{doi} + \verb 10.1016/S0257-8972(02)00853-8 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0257897202008538 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0257897202008538 + \endverb + \keyw{Co-base Stellite alloys,Microstructure and wear resistance,Molybdenum,PTA} + \endentry + \entry{ahmedSlidingWearBlended2021a}{article}{}{} + \name{author}{3}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{652318761812c14e2605b641664892df} + \strng{fullhashraw}{652318761812c14e2605b641664892df} + \strng{bibnamehash}{652318761812c14e2605b641664892df} + \strng{authorbibnamehash}{652318761812c14e2605b641664892df} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{652318761812c14e2605b641664892df} + \strng{authorfullhashraw}{652318761812c14e2605b641664892df} + \field{extraname}{3} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This investigation reports on the tribomechanical evaluations of a Co-based alloy obtained by the hot isostatic pressing (HIPing) of a blend of two standard gas atomized cobalt alloy powders. A HIPed blend of Stellite 6 and Stellite 20 was used to investigate the effect of varying the C, Cr, and W content simultaneously on the structure-property relationships. Microstructural evaluations involved scanning electron microscopy and x-ray diffraction. Experimental evaluations were conducted using hardness, impact, tensile, abrasive wear and sliding wear tests to develop an understanding of the mechanical and tribological performance of the alloys. Results are discussed in terms of the failure modes for the mechanical tests, and wear mechanisms for the tribological tests. This study indicates that powder blends can be used to design for a desired combination of mechanical strength and wear properties in these HIPed alloys. Specific relationships were observed between the alloy composition and carbide content, hardness, impact energy and wear resistance. There was a linear relationship between the weighted W- and C-content and the carbide fraction. The abrasive wear performance also showed a linear relationship with the weighted alloy composition. The pin-on-disc and ball-on-flat experiments revealed a more complex relationship between the alloy composition and the wear rate.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{18 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Sliding wear of blended cobalt based alloys} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{466-467} + \field{year}{2021} + \field{urldateera}{ce} + \field{pages}{203533} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.wear.2020.203533 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164820309923 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164820309923 + \endverb + \keyw{Blending,HIPing,Hardness,Powder metallurgy,Sliding wear,Stellite alloy} + \endentry + \entry{crookCobaltbaseAlloysResist1994}{article}{}{} + \name{author}{1}{}{% + {{hash=16985215fbfc4124567154cd4ca61487}{% + family={Crook}, + familyi={C\bibinitperiod}, + given={P}, + giveni={P\bibinitperiod}}}% + } + \strng{namehash}{16985215fbfc4124567154cd4ca61487} + \strng{fullhash}{16985215fbfc4124567154cd4ca61487} + \strng{fullhashraw}{16985215fbfc4124567154cd4ca61487} + \strng{bibnamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authorbibnamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authornamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authorfullhash}{16985215fbfc4124567154cd4ca61487} + \strng{authorfullhashraw}{16985215fbfc4124567154cd4ca61487} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{issn}{0882-7958} + \field{journaltitle}{Cobalt-base alloys resist wear, corrosion, and heat} + \field{note}{Place: Materials Park, OH Publisher: ASM International} + \field{number}{4} + \field{title}{Cobalt-base alloys resist wear, corrosion, and heat} + \field{volume}{145} + \field{year}{1994} + \field{pages}{27\bibrangedash 30} + \range{pages}{4} + \endentry + \entry{huangMicrostructureEvolutionMartensite2023}{article}{}{} + \name{author}{6}{}{% + {{hash=55328195d8b2c0f90f11e12f5ddb7d65}{% + family={Huang}, + familyi={H\bibinitperiod}, + given={Zonglian}, + giveni={Z\bibinitperiod}}}% + {{hash=2938deb5048323c6e1bfdd80975d5b28}{% + family={Wang}, + familyi={W\bibinitperiod}, + given={Bo}, + giveni={B\bibinitperiod}}}% + {{hash=0138deaf332692ced30d823b9cebc488}{% + family={Liu}, + familyi={L\bibinitperiod}, + given={Fei}, + giveni={F\bibinitperiod}}}% + {{hash=92c4cc87ddf9f0a5abb5ff8d5b8878d4}{% + family={Song}, + familyi={S\bibinitperiod}, + given={Min}, + giveni={M\bibinitperiod}}}% + {{hash=971be18e8809118d44c885580820c916}{% + family={Ni}, + familyi={N\bibinitperiod}, + given={Song}, + giveni={S\bibinitperiod}}}% + {{hash=eb96d2754cddae273dd482f087734e31}{% + family={Liu}, + familyi={L\bibinitperiod}, + given={Shaojun}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{61779e4ce456f415f5dc118db21bed83} + \strng{fullhash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{fullhashraw}{8ca9ebea09cf1f645c339306001d45ac} + \strng{bibnamehash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authorbibnamehash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authornamehash}{61779e4ce456f415f5dc118db21bed83} + \strng{authorfullhash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authorfullhashraw}{8ca9ebea09cf1f645c339306001d45ac} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The influence of laser energy density and heat treatment on the microstructure and properties of Co-Cr-Mo-W alloys fabricated by selective laser melting (SLM) are investigated symmetrically. When the laser power, the scanning speed, and the scanning space are set as 160 W, 400 mm/s, and 0.07 mm, respectively, the SLM-ed Co-Cr-Mo-W alloys display high strength and good ductility simultaneously. The precipitates ranging from nano- to macro- scale are finely distributed in SLM-ed CoCr alloys grains and/or along the grain boundaries in the heat treated alloys. Co-Cr-Mo-W alloys with an excellent combination of strength and ductility can be achieved by tailoring the microstructure and morphology of SLM-ed alloys during the heat treatment. The tensile strength, yield strength, and elongation are 1221.38 ± 10 MPa, 778.81 ± 12 MPa, and 17.2 ± 0.67\%, respectively.} + \field{issn}{0263-4368} + \field{journaltitle}{International Journal of Refractory Metals and Hard Materials} + \field{month}{6} + \field{title}{Microstructure evolution, martensite transformation and mechanical properties of heat treated {Co}-{Cr}-{Mo}-{W} alloys by selective laser melting} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{113} + \field{year}{2023} + \field{urldateera}{ce} + \field{pages}{106170} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.ijrmhm.2023.106170 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0263436823000707 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0263436823000707 + \endverb + \keyw{Co–Cr–Mo-W alloys,Heat treatment,Martensite phase transformation,Mechanical properties,Selective laser melting} + \endentry + \entry{tawancyFccHcpTransformation1986}{article}{}{} + \name{author}{3}{}{% + {{hash=f3547527506994c69c774b2c0d77ac73}{% + family={Tawancy}, + familyi={T\bibinitperiod}, + given={H.\bibnamedelimi M.}, + giveni={H\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=f7d566a34064f3d0ccab33dde7a34069}{% + family={Ishwar}, + familyi={I\bibinitperiod}, + given={V.\bibnamedelimi R.}, + giveni={V\bibinitperiod\bibinitdelim R\bibinitperiod}}}% + {{hash=6f964da88776c95344b60d3d9b6241fa}{% + family={Lewis}, + familyi={L\bibinitperiod}, + given={B.\bibnamedelimi E.}, + giveni={B\bibinitperiod\bibinitdelim E\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \strng{namehash}{4de94c11cde2eac1de960723e9eac321} + \strng{fullhash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{fullhashraw}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{bibnamehash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authorbibnamehash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authornamehash}{4de94c11cde2eac1de960723e9eac321} + \strng{authorfullhash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authorfullhashraw}{b41586e8f4d7f9d36d48a78941a8c3b5} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{issn}{1573-4811} + \field{journaltitle}{Journal of Materials Science Letters} + \field{month}{3} + \field{note}{33 citations (Semantic Scholar/DOI) [2025-04-13]} + \field{number}{3} + \field{title}{On the fcc → hcp transformation in a cobalt-base superalloy ({Haynes} alloy {No}. 25)} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{5} + \field{year}{1986} + \field{urldateera}{ce} + \field{pages}{337\bibrangedash 341} + \range{pages}{5} + \verb{doi} + \verb 10.1007/BF01748098 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/BF01748098 + \endverb + \verb{url} + \verb https://doi.org/10.1007/BF01748098 + \endverb + \keyw{Haynes Alloy,Polymer,Polymers} + \endentry + \entry{yuComparisonTriboMechanicalProperties2007}{article}{}{} + \name{author}{3}{}{% + {{hash=f46cff6a47143fdbd36ae8842919e073}{% + family={Yu}, + familyi={Y\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=39fbce992265c4dd42ff7cb6ab804ded}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + } + \strng{namehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{fullhash}{8e67a0a25c7114030e7e739ed034990b} + \strng{fullhashraw}{8e67a0a25c7114030e7e739ed034990b} + \strng{bibnamehash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authorbibnamehash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authornamehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{authorfullhash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authorfullhashraw}{8e67a0a25c7114030e7e739ed034990b} + \field{extraname}{1} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This paper aims to compare the tribo-mechanical properties and structure–property relationships of a wear resistant cobalt-based alloy produced via two different manufacturing routes, namely sand casting and powder consolidation by hot isostatic pressing (HIPing). The alloy had a nominal wt \% composition of Co–33Cr–17.5W–2.5C, which is similar to the composition of commercially available Stellite 20 alloy. The high tungsten and carbon contents provide resistance to severe abrasive and sliding wear. However, the coarse carbide structure of the cast alloy also gives rise to brittleness. Hence this research was conducted to comprehend if the carbide refinement and corresponding changes in the microstructure, caused by changing the processing route to HIPing, could provide additional merits in the tribo-mechanical performance of this alloy. The HIPed alloy possessed a much finer microstructure than the cast alloy. Both alloys had similar hardness, but the impact resistance of the HIPed alloy was an order of magnitude higher than the cast counterpart. Despite similar abrasive and sliding wear resistance of both alloys, their main wear mechanisms were different due to their different carbide morphologies. Brittle fracture of the carbides and ploughing of the matrix were the main wear mechanisms for the cast alloy, whereas ploughing and carbide pullout were the dominant wear mechanisms for the HIPed alloy. The HIPed alloy showed significant improvement in contact fatigue performance, indicating its superior impact and fatigue resistance without compromising the hardness and sliding∕abrasive wear resistance, which makes it suitable for relatively higher stress applications.} + \field{issn}{0742-4787} + \field{journaltitle}{Journal of Tribology} + \field{month}{1} + \field{note}{37 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{3} + \field{title}{A {Comparison} of the {Tribo}-{Mechanical} {Properties} of a {Wear} {Resistant} {Cobalt}-{Based} {Alloy} {Produced} by {Different} {Manufacturing} {Processes}} + \field{urlday}{17} + \field{urlmonth}{11} + \field{urlyear}{2024} + \field{volume}{129} + \field{year}{2007} + \field{urldateera}{ce} + \field{pages}{586\bibrangedash 594} + \range{pages}{9} + \verb{doi} + \verb 10.1115/1.2736450 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1115/1.2736450 + \endverb + \verb{url} + \verb https://doi.org/10.1115/1.2736450 + \endverb + \endentry + \entry{stoicaInfluenceHeattreatmentSliding2005}{article}{}{} + \name{author}{3}{}{% + {{hash=9ee308ed1264406c99dc3dc19fc74bbc}{% + family={Stoica}, + familyi={S\bibinitperiod}, + given={V.}, + giveni={V\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=396db0229b4cd75917372e6b8a4c12ee}{% + family={Itsukaichi}, + familyi={I\bibinitperiod}, + given={T.}, + giveni={T\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{1dad3e925506f0bfcbc611fb083a4a04} + \strng{fullhash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{fullhashraw}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{bibnamehash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authorbibnamehash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authornamehash}{1dad3e925506f0bfcbc611fb083a4a04} + \strng{authorfullhash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authorfullhashraw}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Functionally graded WC-NiCrBSi coatings were thermally sprayed using a High Velocity Oxy-Fuel (JP5000) system and heat-treated at 1200 °C in argon environment. The relative performance of the as-sprayed and heat-treated coatings was investigated in sliding wear under different tribological conditions of contact stress, and test couple configuration, using a high frequency reciprocating ball on plate rig. Test results are discussed with the help of microstructural evaluations and mechanical properties measurements. Results indicate that by heat-treating the coatings at a temperature of 1200 °C, it is possible to achieve higher wear resistance, both in terms of coating wear, as well as the total wear of the test couples. This was attributed to the improvements in the coating microstructure during the heat-treatment, which resulted in an improvement in coating's mechanical properties through the formation of hard phases, elimination of brittle W2C and W, and the establishment of metallurgical bonding within the coating microstructure. © 2005 Elsevier B.V. All rights reserved.} + \field{issn}{02578972 (ISSN)} + \field{journaltitle}{Surface and Coatings Technology} + \field{note}{41 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{title}{Influence of heat-treatment on the sliding wear of thermal spray cermet coatings} + \field{volume}{199} + \field{year}{2005} + \field{pages}{7\bibrangedash 21} + \range{pages}{15} + \verb{doi} + \verb 10.1016/j.surfcoat.2005.03.026 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-21844464044&doi=10.1016%2fj.surfcoat.2005.03.026&partnerID=40&md5=6ad736723e828d39edf4a37c5975d2dc + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-21844464044&doi=10.1016%2fj.surfcoat.2005.03.026&partnerID=40&md5=6ad736723e828d39edf4a37c5975d2dc + \endverb + \keyw{Bonding,Brittleness,Cermets,Coating microstructure,Frequencies,Functionally graded materials,Heat treatment,Heat-treated coatings,Heat-treatment,High Velocity Oxy-Fuel,Mechanical properties,Microstructure,Nickel compounds,Phase composition,Sliding wear,Sprayed coatings,Thermal spray coatings,Tribology,Tungsten compounds,Wear of materials,heat treatment,sliding wear} + \endentry + \entry{ahmedInfluenceReHIPingStructure2013}{article}{}{} + \name{author}{4}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + {{hash=1c8f35a67217a8f6cbd1f8d3edb797b0}{% + family={Faisal}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi H.}, + giveni={N\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{fullhashraw}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{bibnamehash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authorbibnamehash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authorfullhashraw}{e70fdd408b4a5e9730bd0722565b8e34} + \field{extraname}{4} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{HIP-consolidation (Hot Isostatic Pressing or HIPing) of cobalt-based Stellite alloys offers significant technological advantages for components operating in aggressive wear environments. The aim of this investigation was to ascertain the effect of re-HIPing on the HIPed alloy properties for Stellite 4, 6 and 20 alloys. Structure–property relationships are discussed on the basis of microstructural and tribo-mechanical evaluations. Re-HIPing results in coarsening of carbides and solid solution strengthening of the matrix. The average indentation modulus improved, as did the average hardness at micro- and nano-scales. Re-HIPing showed improvement in wear properties the extent of which was dependent on alloy composition.} + \field{issn}{0301-679X} + \field{journaltitle}{Tribology International} + \field{month}{1} + \field{note}{38 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Influence of {Re}-{HIPing} on the structure–property relationships of cobalt-based alloys} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{57} + \field{year}{2013} + \field{urldateera}{ce} + \field{pages}{8\bibrangedash 21} + \range{pages}{14} + \verb{doi} + \verb 10.1016/j.triboint.2012.06.025 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X12002241 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X12002241 + \endverb + \keyw{Abrasive wear,Cobalt based alloys,HIPing and Re-HIPing,Stellite 4,6,20,alloys} + \endentry + \entry{yuInfluenceManufacturingProcess2008}{article}{}{} + \name{author}{4}{}{% + {{hash=f46cff6a47143fdbd36ae8842919e073}{% + family={Yu}, + familyi={Y\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=720a4573d41f2302c51d8dfc20eb7025}{% + family={Lovelock}, + familyi={L\bibinitperiod}, + given={H.\bibnamedelimi de\bibnamedelima Villiers}, + giveni={H\bibinitperiod\bibinitdelim d\bibinitperiod\bibinitdelim V\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{fullhash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{fullhashraw}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{bibnamehash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authorbibnamehash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authornamehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{authorfullhash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authorfullhashraw}{57ca415fdcbe0d531a76658a78b7a3d4} + \field{extraname}{2} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Manufacturing process routes of materials can be adapted to manipulate their microstructure and hence their tribological performance. As industrial demands push the applications of tribological materials to harsher environments of higher stress, starved lubrication, and improved life performance, manufacturing processes can be tailored to optimize their use in particular engineering applications. The aim of this paper was therefore to comprehend the structure-property relationships of a wear resistant cobalt-based alloy (Stellite 6) produced from two different processing routes of powder consolidated hot isostatic pressing (HIPing) and casting. This alloy had a nominal wt \% composition of Co–28Cr–4.5W–1C, which is commonly used in wear related applications in harsh tribological environments. However, the coarse carbide structure of the cast alloy results in higher brittleness and lower toughness. Hence this research was conducted to comprehend if carbide refinement, caused by changing the processing route to HIPing, could improve the tribomechanical performance of this alloy. Microstructural and tribomechanical evaluations, which involved hardness, impact toughness, abrasive wear, sliding wear, and contact fatigue performance tests, indicated that despite the similar abrasive and sliding wear resistance of both alloys, the HIPed alloy exhibited an improved contact fatigue and impact toughness performance in comparison to the cast counterpart. This difference in behavior is discussed in terms of the structure-property relationships. Results of this research indicated that the HIPing process could provide additional impact and fatigue resistance to this alloy without compromising the hardness and the abrasive/sliding wear resistance, which makes the HIPed alloy suitable for relatively higher stress applications. Results are also compared with a previously reported investigation of the Stellite 20 alloy, which had a much higher carbide content in comparison to the Stellite 6 alloy, caused by the variation in the content of alloying elements. These results indicated that the fatigue resistance did not follow the expected trend of the improvement in impact toughness. In terms of the design process, the combination of hardness, toughness, and carbide content show a complex interdependency, where a 40\% reduction in the average hardness and 60\% reduction in carbide content had a more dominating effect on the contact fatigue resistance when compared with an order of magnitude improvement in the impact toughness of the HIPed Stellite 6 alloy.} + \field{issn}{0742-4787} + \field{journaltitle}{Journal of Tribology} + \field{month}{12} + \field{note}{46 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{011601} + \field{title}{Influence of {Manufacturing} {Process} and {Alloying} {Element} {Content} on the {Tribomechanical} {Properties} of {Cobalt}-{Based} {Alloys}} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{131} + \field{year}{2008} + \field{urldateera}{ce} + \verb{doi} + \verb 10.1115/1.2991122 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1115/1.2991122 + \endverb + \verb{url} + \verb https://doi.org/10.1115/1.2991122 + \endverb + \endentry + \entry{szalaEffectNitrogenIon2021}{article}{}{} + \name{author}{6}{}{% + {{hash=26ecda2187f0e2b702a2497a5dc3f27d}{% + family={Szala}, + familyi={S\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + {{hash=b1f8638f62fc396f39212102aa9a7be4}{% + family={Chocyk}, + familyi={C\bibinitperiod}, + given={D.}, + giveni={D\bibinitperiod}}}% + {{hash=fa359615394426dff04c6f196de50a92}{% + family={Skic}, + familyi={S\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + {{hash=735ac71614372e54c2c5b12c4a8b2037}{% + family={Kamiński}, + familyi={K\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + {{hash=80f5de14d028c35ed21c52a0993eb44e}{% + family={Macek}, + familyi={M\bibinitperiod}, + given={W.}, + giveni={W\bibinitperiod}}}% + {{hash=2458b153bc1351893a163117b0b687eb}{% + family={Turek}, + familyi={T\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{0c580510ffd19c48fb276fd9bcbd3cc8} + \strng{fullhash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{fullhashraw}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{bibnamehash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authorbibnamehash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authornamehash}{0c580510ffd19c48fb276fd9bcbd3cc8} + \strng{authorfullhash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authorfullhashraw}{ed8bfd0d39c94dcd76e642641bd4b638} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{From the wide range of engineering materials traditional Stellite 6 (cobalt alloy) exhibits excellent resistance to cavitation erosion (CE). Nonetheless, the influence of ion implantation of cobalt alloys on the CE behaviour has not been completely clarified by the literature. Thus, this work investigates the effect of nitrogen ion implantation (NII) of HIPed Stellite 6 on the improvement of resistance to CE. Finally, the cobalt-rich matrix phase transformations due to both NII and cavitation load were studied. The CE resistance of stellites ion-implanted by 120 keV N+ ions two fluences: 5*1016 cm-2 and 1*1017 cm-2 were comparatively analysed with the unimplanted stellite and AISI 304 stainless steel. CE tests were conducted according to ASTM G32 with stationary specimen method. Erosion rate curves and mean depth of erosion confirm that the nitrogen-implanted HIPed Stellite 6 two times exceeds the resistance to CE than unimplanted stellite, and has almost ten times higher CE reference than stainless steel. The X-ray diffraction (XRD) confirms that NII of HIPed Stellite 6 favours transformation of the "(hcp) to (fcc) structure. Unimplanted stellite "-rich matrix is less prone to plastic deformation than and consequently, increase of phase effectively holds carbides in cobalt matrix and prevents Cr7C3 debonding. This phenomenon elongates three times the CE incubation stage, slows erosion rate and mitigates the material loss. Metastable structure formed by ion implantation consumes the cavitation load for work-hardening and ! " martensitic transformation. In further CE stages, phases transform as for unimplanted alloy namely, the cavitation-inducted recovery process, removal of strain, dislocations resulting in increase of phase. The CE mechanism was investigated using a surface profilometer, atomic force microscopy, SEM-EDS and XRD. HIPed Stellite 6 wear behaviour relies on the plastic deformation of cobalt matrix, starting at Cr7C3/matrix interfaces. Once the Cr7C3 particles lose from the matrix restrain, they debond from matrix and are removed from the material. Carbides detachment creates cavitation pits which initiate cracks propagation through cobalt matrix, that leads to loss of matrix phase and as a result the CE proceeds with a detachment of massive chunk of materials. © 2021 by the authors.} + \field{issn}{19961944 (ISSN)} + \field{journaltitle}{Materials} + \field{note}{Publisher: MDPI AG} + \field{number}{9} + \field{title}{Effect of nitrogen ion implantation on the cavitation erosion resistance and cobalt-based solid solution phase transformations of {HIPed} stellite 6} + \field{volume}{14} + \field{year}{2021} + \verb{doi} + \verb 10.3390/ma14092324 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-85105941706&doi=10.3390%2fma14092324&partnerID=40&md5=4c846be7d06977d42697c88c326e5923 + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-85105941706&doi=10.3390%2fma14092324&partnerID=40&md5=4c846be7d06977d42697c88c326e5923 + \endverb + \keyw{AISI-304 stainless steel,Atomic force microscopy,Carbides,Cavitation,Cavitation erosion,Cavitation erosion resistance,Chromium compounds,Cobalt alloy,Cobalt alloys,Cracks propagation,Damage mechanism,Engineering materials,Erosion,Failure analysis,Ion implantation,Ions,Linear transformations,Martensitic transformations,Mean depth of erosions,Metastable structures,Nitrogen,Nitrogen ion implantations,Phase transformation,Plastic deformation,Stellite,Stellite 6,Strain hardening,Surface profilometers,Wear,X ray diffraction} + \endentry + \entry{thiruvengadamTheoryErosion1967}{article}{}{} + \name{author}{1}{}{% + {{hash=d3cae98a50611da092efbc498a5a497c}{% + family={Thiruvengadam}, + familyi={T\bibinitperiod}, + given={Alagu}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{d3cae98a50611da092efbc498a5a497c} + \strng{fullhash}{d3cae98a50611da092efbc498a5a497c} + \strng{fullhashraw}{d3cae98a50611da092efbc498a5a497c} + \strng{bibnamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorbibnamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authornamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorfullhash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorfullhashraw}{d3cae98a50611da092efbc498a5a497c} + \field{sortinit}{6} + \field{sortinithash}{b33bc299efb3c36abec520a4c896a66d} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{An elementary theory of erosion is derived based on the assumptions of 'accumulation' and 'attenuation' of the energies of impact causing erosion. This theory quantitatively predicts the relative intensity of erosion as a function of relative time and this prediction is in fair agreement with experimental observations. Since the intensity of collision, the distance of shock transmission and the material failure are all statistical events, a generalization of the elementary theory is suggested. Some of the practical results of this theory are the predictions of the cumulative depth of erosion, the determination of erosion strength and the method of correlation with other parameters such as liquid properties and hydrodynamic factors. Modifications of this theory for brittle and viscoelastic materials are also suggested. (Author)} + \field{journaltitle}{Proc. 2nd Meersburg Conf. on Rain Erosion and Allied Phenomena} + \field{month}{3} + \field{title}{Theory of erosion} + \field{volume}{2} + \field{year}{1967} + \field{pages}{53} + \range{pages}{1} + \endentry + \enddatalist +\endrefsection + +\refsection{1} + \datalist[entry]{none/global//global/global/global} + \entry{C05}{misc}{}{} + \name{author}{1}{}{% + {{hash=fc13b91fcf8c46eeb4e62740272a1ba9}{% + family={Awesome}, + familyi={A\bibinitperiod}, + given={F.}, + giveni={F\bibinitperiod}}}% + } + \strng{namehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{bibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorbibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authornamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \field{extraname}{1} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{title}{Frank} + \field{year}{2005} + \true{nocite} + \keyw{mine} + \endentry + \entry{C06}{misc}{}{} + \name{author}{1}{}{% + {{hash=fc13b91fcf8c46eeb4e62740272a1ba9}{% + family={Awesome}, + familyi={A\bibinitperiod}, + given={F.}, + giveni={F\bibinitperiod}}}% + } + \strng{namehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{bibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorbibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authornamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \field{extraname}{2} + \field{sortinit}{3} + \field{sortinithash}{ad6fe7482ffbd7b9f99c9e8b5dccd3d7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{title}{frank, but lowercase} + \field{year}{2006} + \true{nocite} + \keyw{mine} + \endentry + \enddatalist +\endrefsection +\endinput + diff --git a/Thesis.bbl-SAVE-ERROR b/Thesis.bbl-SAVE-ERROR new file mode 100644 index 0000000..4bcac41 --- /dev/null +++ b/Thesis.bbl-SAVE-ERROR @@ -0,0 +1,1568 @@ +% $ biblatex auxiliary file $ +% $ biblatex bbl format version 3.3 $ +% Do not modify the above lines! +% +% This is an auxiliary file used by the 'biblatex' package. +% This file may safely be deleted. It will be recreated by +% biber as required. +% +\begingroup +\makeatletter +\@ifundefined{ver@biblatex.sty} + {\@latex@error + {Missing 'biblatex' package} + {The bibliography requires the 'biblatex' package.} + \aftergroup\endinput} + {} +\endgroup + + +\refsection{0} + \datalist[entry]{none/global//global/global/global} + \entry{ahmedStructurePropertyRelationships2014}{article}{}{} + \name{author}{4}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=1c8f35a67217a8f6cbd1f8d3edb797b0}{% + family={Faisal}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi H.}, + giveni={N\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{fullhashraw}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{bibnamehash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authorbibnamehash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{0ba22f8fbb626d88357e4651c3f66f4d} + \strng{authorfullhashraw}{0ba22f8fbb626d88357e4651c3f66f4d} + \field{extraname}{1} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This investigation considered the multiscale tribo-mechanical evaluations of CoCrMo (Stellite®21) alloys manufactured via two different processing routes of casting and HIP-consolidation from powder (Hot Isostatic Pressing). These involved hardness, nanoscratch, impact toughness, abrasive wear and sliding wear evaluations using pin-on-disc and ball-on-flat tests. HIPing improved the nanoscratch and ball-on-flat sliding wear performance due to higher hardness and work-hardening rate of the metal matrix. The cast alloy however exhibited superior abrasive wear and self-mated pin-on-disc wear performance. The tribological properties were more strongly influenced by the CoCr matrix, which is demonstrated in nanoscratch analysis.} + \field{issn}{0301-679X} + \field{journaltitle}{Tribology International} + \field{month}{12} + \field{note}{24 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Structure–property relationships in a {CoCrMo} alloy at micro and nano-scales} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{80} + \field{year}{2014} + \field{urldateera}{ce} + \field{pages}{98\bibrangedash 114} + \range{pages}{17} + \verb{doi} + \verb 10.1016/j.triboint.2014.06.015 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X14002436 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X14002436 + \endverb + \keyw{Manufacturing,Nanoscratch,Nanotribology,Wear} + \endentry + \entry{malayogluComparingPerformanceHIPed2003}{article}{}{} + \name{author}{2}{}{% + {{hash=71f57eb10950396ed3fa62c703ddaee5}{% + family={Malayoglu}, + familyi={M\bibinitperiod}, + given={U.}, + giveni={U\bibinitperiod}}}% + {{hash=c00a172220606f67c3da2492047a9b71}{% + family={Neville}, + familyi={N\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{fullhash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{fullhashraw}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{bibnamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorbibnamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authornamehash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorfullhash}{49054a18ed24a57daa4c3278c94c6ce5} + \strng{authorfullhashraw}{49054a18ed24a57daa4c3278c94c6ce5} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In this paper, results from erosion–corrosion tests performed under liquid–solid erosion conditions in 3.5\% NaCl liquid medium are reported. The focus of the paper is to compare the behaviour of Cast and Hot Isostatically Pressed (HIPed) Stellite 6 alloy in terms of their electrochemical corrosion characteristics, their resistance to mechanical degradation and relationship between microstructure and degradation mechanisms. It has been shown that HIPed Stellite 6 possesses better erosion and erosion corrosion resistance than that of Cast Stellite 6 and two stainless steels (UNS S32760 and UNS S31603) under the same solid loading (200 and 500mg/l), and same temperature (20 and 50°C). The material removal mechanisms have been identified by using atomic force microscopy (AFM) and shown preferential removal of the Co-rich matrix to be less extensive on the HIPed material.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{8} + \field{note}{34 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{series}{14th {International} {Conference} on {Wear} of {Materials}} + \field{title}{Comparing the performance of {HIPed} and {Cast} {Stellite} 6 alloy in liquid–solid slurries} + \field{urlday}{17} + \field{urlmonth}{2} + \field{urlyear}{2025} + \field{volume}{255} + \field{year}{2003} + \field{urldateera}{ce} + \field{pages}{181\bibrangedash 194} + \range{pages}{14} + \verb{doi} + \verb 10.1016/S0043-1648(03)00287-4 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164803002874 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164803002874 + \endverb + \keyw{Cast Stellite 6,Corrosion,Erosion,HIPed,Liquid–solid slurries} + \endentry + \entry{davis2000nickel}{book}{}{} + \name{author}{2}{}{% + {{hash=d24975e937cc4c8eafeb981d8d16a1d4}{% + family={Davis}, + familyi={D\bibinitperiod}, + given={J.R.}, + giveni={J\bibinitperiod}}}% + {{hash=2e482fdb03378296689bc75a76c2bdc4}{% + family={Committee}, + familyi={C\bibinitperiod}, + given={A.S.M.I.H.}, + giveni={A\bibinitperiod}}}% + } + \list{publisher}{1}{% + {ASM International}% + } + \strng{namehash}{ded5e703628bfa51629c3e9340068998} + \strng{fullhash}{ded5e703628bfa51629c3e9340068998} + \strng{fullhashraw}{ded5e703628bfa51629c3e9340068998} + \strng{bibnamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authorbibnamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authornamehash}{ded5e703628bfa51629c3e9340068998} + \strng{authorfullhash}{ded5e703628bfa51629c3e9340068998} + \strng{authorfullhashraw}{ded5e703628bfa51629c3e9340068998} + \field{sortinit}{3} + \field{sortinithash}{ad6fe7482ffbd7b9f99c9e8b5dccd3d7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{isbn}{978-0-87170-685-0} + \field{note}{tex.lccn: 00059348} + \field{series}{{ASM} specialty handbook} + \field{title}{Nickel, cobalt, and their alloys} + \field{year}{2000} + \verb{urlraw} + \verb https://books.google.ae/books?id=IePhmnbmRWkC + \endverb + \verb{url} + \verb https://books.google.ae/books?id=IePhmnbmRWkC + \endverb + \endentry + \entry{alimardaniEffectLocalizedDynamic2010}{article}{}{} + \name{author}{4}{}{% + {{hash=b1d020be51ce7b141b4cf03868da762c}{% + family={Alimardani}, + familyi={A\bibinitperiod}, + given={Masoud}, + giveni={M\bibinitperiod}}}% + {{hash=44e10f283ada211ed0a7aa6d9913d23f}{% + family={Fallah}, + familyi={F\bibinitperiod}, + given={Vahid}, + giveni={V\bibinitperiod}}}% + {{hash=5aaf85cb279ac1471a04ce9c932a1122}{% + family={Khajepour}, + familyi={K\bibinitperiod}, + given={Amir}, + giveni={A\bibinitperiod}}}% + {{hash=88451951b0b3c1cc4383d3cebfc151ac}{% + family={Toyserkani}, + familyi={T\bibinitperiod}, + given={Ehsan}, + giveni={E\bibinitperiod}}}% + } + \strng{namehash}{86846ed827567cfd839f7c014178ad64} + \strng{fullhash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{fullhashraw}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{bibnamehash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authorbibnamehash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authornamehash}{86846ed827567cfd839f7c014178ad64} + \strng{authorfullhash}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \strng{authorfullhashraw}{6d9fe21dc14c2e93f67f0a8f73f5082f} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In laser cladding, high cooling rates create outcomes with superior mechanical and metallurgical properties. However, this characteristic along with the additive nature of the process significantly contributes to the formation of thermal stresses which are the main cause of any potential delamination and crack formation across the deposited layers. This drawback is more prominent for additive materials such as Stellite 1 which are by nature crack-sensitive during the hardfacing process. In this work, parallel to the experimental investigation, a numerical model is used to study the temperature distributions and thermal stresses throughout the deposition of Stellite 1 for hardfacing application. To manage the thermal stresses, the effect of preheating the substrate in a localized dynamic fashion is investigated. The numerical and experimental analyses are conducted by the deposition of Stellite 1 powder on the substrate of AISI-SAE 4340 alloy steel using a 1.1kW fiber laser. Experimental results confirm that by preheating the substrate a crack-free coating layer of Stellite 1 well-bonded to the substrate with a uniform dendritic structure, well-distributed throughout the deposited layer, can be obtained contrary to non-uniform structures formed in the coating of the non-preheated substrate with several cracks.} + \field{issn}{0257-8972} + \field{journaltitle}{Surface and Coatings Technology} + \field{month}{8} + \field{note}{64 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{23} + \field{title}{The effect of localized dynamic surface preheating in laser cladding of {Stellite} 1} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{204} + \field{year}{2010} + \field{urldateera}{ce} + \field{pages}{3911\bibrangedash 3919} + \range{pages}{9} + \verb{doi} + \verb 10.1016/j.surfcoat.2010.05.009 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0257897210003701 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0257897210003701 + \endverb + \keyw{Crack formation,Hardfacing alloys,Laser cladding,Preheating process,Temperature and thermal stress fields} + \endentry + \entry{ahmedMappingMechanicalProperties2023}{article}{}{} + \name{author}{3}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=8da5f61983121a25e044ca92bd036b2a}{% + family={Fardan}, + familyi={F\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{fullhashraw}{b3a15b2b31620e3640b3b3a16271687c} + \strng{bibnamehash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authorbibnamehash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{b3a15b2b31620e3640b3b3a16271687c} + \strng{authorfullhashraw}{b3a15b2b31620e3640b3b3a16271687c} + \field{extraname}{2} + \field{sortinit}{6} + \field{sortinithash}{b33bc299efb3c36abec520a4c896a66d} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Stellite alloys have good wear resistance and maintain their strength up to 600°C, making them suitable for various industrial applications like cutting tools and combustion engine parts. This investigation was aimed at i) manufacturing new Stellite alloy blends using powder metallurgy and ii) mathematically mapping hardness, yield strength, ductility and impact energy of base and alloy blends. Linear, exponential, polynomial approximations and dimensional analyses were conducted in this semi-empirical mathematical modelling approach. Base alloy compositions similar to Stellite 1, 4, 6, 12, 20 and 190 were used in this investigation to form new alloys via blends. The microstructure was analysed using Scanning Electron Microscopy (SEM) and X-ray Diffraction (XRD). Mechanical performance of alloys was conducted using tensile, hardness and Charpy impact tests. MATLAB® coding was used for the development of property maps. This investigation indicates that hardness and yield strength can be linked to the wt.\% composition of carbon and tungsten using linear approximation with a maximum variance of 5\% and 20\%, respectively. Elongation and carbide fraction showed a non-linear relationship with alloy composition. Impact energy was linked with elongation through polynomial approximation. A dimensional analysis was developed by interlinking carbide fraction, hardness, yield strength, and elongation to impact energy.} + \field{issn}{2374-068X} + \field{journaltitle}{Advances in Materials and Processing Technologies} + \field{month}{6} + \field{note}{1 citations (Semantic Scholar/DOI) [2025-04-12] Publisher: Taylor \& Francis \_eprint: https://doi.org/10.1080/2374068X.2023.2220242} + \field{number}{0} + \field{title}{Mapping the mechanical properties of cobalt-based stellite alloys manufactured via blending} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{0} + \field{year}{2023} + \field{urldateera}{ce} + \field{pages}{1\bibrangedash 30} + \range{pages}{30} + \verb{doi} + \verb 10.1080/2374068X.2023.2220242 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1080/2374068X.2023.2220242 + \endverb + \verb{url} + \verb https://doi.org/10.1080/2374068X.2023.2220242 + \endverb + \keyw{Blending,Hiping,Mathematical model,Powder metallurgy,Stellite alloys,Structure-property relationships} + \endentry + \entry{bunchCorrosionGallingResistant1989}{inproceedings}{}{} + \name{author}{3}{}{% + {{hash=ff8de9c468efb7eab8b92e573d3949ed}{% + family={Bunch}, + familyi={B\bibinitperiod}, + given={P.\bibnamedelimi O.}, + giveni={P\bibinitperiod\bibinitdelim O\bibinitperiod}}}% + {{hash=47f88033d1313a3ac56378baefb344e4}{% + family={Hartmann}, + familyi={H\bibinitperiod}, + given={M.\bibnamedelimi P.}, + giveni={M\bibinitperiod\bibinitdelim P\bibinitperiod}}}% + {{hash=7f4198582fc42b8ddab60cd433790594}{% + family={Bednarowicz}, + familyi={B\bibinitperiod}, + given={T.\bibnamedelimi A.}, + giveni={T\bibinitperiod\bibinitdelim A\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \list{publisher}{1}{% + {OnePetro}% + } + \strng{namehash}{b4088224b2a9ea87c42c7ab641ebe2de} + \strng{fullhash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{fullhashraw}{27ba512d074ac1ae4276e7a91ea23549} + \strng{bibnamehash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authorbibnamehash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authornamehash}{b4088224b2a9ea87c42c7ab641ebe2de} + \strng{authorfullhash}{27ba512d074ac1ae4276e7a91ea23549} + \strng{authorfullhashraw}{27ba512d074ac1ae4276e7a91ea23549} + \field{sortinit}{7} + \field{sortinithash}{108d0be1b1bee9773a1173443802c0a3} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{ABSTRACT. Application of corrosion resistant hardfacing materials are required to maintain exceptional reliability for metal to metal sealing in high pressure gate valves used for offshore production wells. New hardfacing materials have been developed and tailored for use where defense against degradation effects of high temperature, high pressure, H2S, C02, free sulfur and brine environments is required. Using a plasma transferred arc (PTA) weld process, new hardfacings of Stellite cobalt base materials have been successfully applied to nickel base alloy substrates. These hardfacings provide exceptional corrosion resistance over previously used materials produced by spray and fuse as well as high velocity combustion spray (} + \field{month}{5} + \field{note}{1 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Corrosion/{Galling} {Resistant} {Hardfacing} {Materials} for {Offshore} {Production} {Valves}} + \field{urlday}{1} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{year}{1989} + \field{urldateera}{ce} + \verb{doi} + \verb 10.4043/6070-MS + \endverb + \verb{urlraw} + \verb https://dx.doi.org/10.4043/6070-MS + \endverb + \verb{url} + \verb https://dx.doi.org/10.4043/6070-MS + \endverb + \endentry + \entry{ratiaComparisonSlidingWear2019}{article}{}{} + \name{author}{7}{}{% + {{hash=4d8d77bd60a2e1fd293e809631bc5a84}{% + family={Ratia}, + familyi={R\bibinitperiod}, + given={Vilma\bibnamedelima L.}, + giveni={V\bibinitperiod\bibinitdelim L\bibinitperiod}}}% + {{hash=84a91dba5410e2e8f67915c4c17aea08}{% + family={Zhang}, + familyi={Z\bibinitperiod}, + given={Deen}, + giveni={D\bibinitperiod}}}% + {{hash=f9e5a7fad20d40241ed0f25f05849207}{% + family={Carrington}, + familyi={C\bibinitperiod}, + given={Matthew\bibnamedelima J.}, + giveni={M\bibinitperiod\bibinitdelim J\bibinitperiod}}}% + {{hash=a61a195bd0ed9f39c9d446f02d7b9592}{% + family={Daure}, + familyi={D\bibinitperiod}, + given={Jaimie\bibnamedelima L.}, + giveni={J\bibinitperiod\bibinitdelim L\bibinitperiod}}}% + {{hash=d9e3c0caaa2d6903c488a2973cea1fd8}{% + family={McCartney}, + familyi={M\bibinitperiod}, + given={D.\bibnamedelimi Graham}, + giveni={D\bibinitperiod\bibinitdelim G\bibinitperiod}}}% + {{hash=d69de7eb40c8f8c0c78825838cd1f8ee}{% + family={Shipway}, + familyi={S\bibinitperiod}, + given={Philip\bibnamedelima H.}, + giveni={P\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=b150a22a65dc3516b89a2bd86a0e25ff}{% + family={Stewart}, + familyi={S\bibinitperiod}, + given={David\bibnamedelima A.}, + giveni={D\bibinitperiod\bibinitdelim A\bibinitperiod}}}% + } + \strng{namehash}{0f5fdf8e51bf5515e4025351773003d8} + \strng{fullhash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{fullhashraw}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{bibnamehash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authorbibnamehash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authornamehash}{0f5fdf8e51bf5515e4025351773003d8} + \strng{authorfullhash}{2e0376be46be3b8d245d5ab5620f4ca2} + \strng{authorfullhashraw}{2e0376be46be3b8d245d5ab5620f4ca2} + \field{sortinit}{8} + \field{sortinithash}{a231b008ebf0ecbe0b4d96dcc159445f} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Cobalt-based alloys such as Stellite 3 and Stellite 6 are widely used to protect stainless steel surfaces in primary circuit nuclear reactor applications where high resistance to wear and corrosion are required. In this study, self-mated sliding wear of Stellite 3 and Stellite 6 consolidated by hot isostatic pressing were compared. Tests were performed with a pin-on-disc apparatus enclosed in a water-submerged autoclave environment and wear was measured from room temperature up to 250 °C (a representative pressurized water reactor environment). Both alloys exhibit a microstructure of micron-sized carbides embedded in a cobalt-rich matrix. Stellite 3 (higher tungsten and carbon content) contains M7C3 and an eta (η) -carbide whereas Stellite 6 contains only M7C3. Furthermore, the former has a significantly higher carbide volume fraction and hardness than the latter. Both alloys show a significant increase in the wear rate as the temperature is increased but Stellite 3 has a higher wear resistance over the entire range; at 250 °C the wear rate of Stellite 6 is more than five times that of Stellite 3. There is only a minimal formation of a transfer layer on the sliding surfaces but electron backscatter diffraction on cross-sections through the wear scar revealed that wear causes partial transformation of the cobalt matrix from fcc to hcp in both alloys over the entire temperature range. It is proposed that the acceleration of wear with increasing temperature in the range studied is associated with a tribocorrosion mechanism and that the higher carbide fraction in Stellite 3 resulted in its reduced wear rate compared to Stellite 6.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{4} + \field{note}{20 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{series}{22nd {International} {Conference} on {Wear} of {Materials}} + \field{title}{Comparison of the sliding wear behaviour of self-mated {HIPed} {Stellite} 3 and {Stellite} 6 in a simulated {PWR} water environment} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{426-427} + \field{year}{2019} + \field{urldateera}{ce} + \field{pages}{1222\bibrangedash 1232} + \range{pages}{11} + \verb{doi} + \verb 10.1016/j.wear.2019.01.116 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S004316481930211X + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S004316481930211X + \endverb + \keyw{Cobalt-based alloys,Electron backscatter diffraction,HIP,Nuclear,Stellite} + \endentry + \entry{zhangFrictionWearCharacterization2002}{article}{}{} + \name{author}{2}{}{% + {{hash=9ac5c6e1891a9d327b6cf9dce9924eaa}{% + family={Zhang}, + familyi={Z\bibinitperiod}, + given={K}, + giveni={K\bibinitperiod}}}% + {{hash=cb8741204d7e12b6db11ee35f025c97c}{% + family={Battiston}, + familyi={B\bibinitperiod}, + given={L}, + giveni={L\bibinitperiod}}}% + } + \strng{namehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{fullhash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{fullhashraw}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{bibnamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorbibnamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authornamehash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorfullhash}{bf171f4e97c3179e4c0d9908cf319a1f} + \strng{authorfullhashraw}{bf171f4e97c3179e4c0d9908cf319a1f} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{A full-journal submerged bearing test rig was built to evaluate the friction and wear behavior of materials in zinc alloy baths. Some cobalt- and iron-based superalloys were tested using this rig at conditions similar to those of a continuous galvanizing operation (load and bath chemistry). Metallographic and chemical analyses were conducted on tested samples to characterize the wear. It was found that a commonly used cobalt-based material (Stellite \#6) not only suffered considerable wear but also reacted with zinc baths to form intermetallic compounds. Other cobalt- and iron-based superalloys appeared to have negligible reaction with the zinc baths in the short-term tests, but cracks developed in the sub-surface, suggesting that the materials mainly experienced surface fatigue wear. The commonly used cobalt-based superalloy mostly experienced abrasive wear.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{33 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{3} + \field{title}{Friction and wear characterization of some cobalt- and iron-based superalloys in zinc alloy baths} + \field{urlday}{1} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{252} + \field{year}{2002} + \field{urldateera}{ce} + \field{pages}{332\bibrangedash 344} + \range{pages}{13} + \verb{doi} + \verb 10.1016/S0043-1648(01)00889-4 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164801008894 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164801008894 + \endverb + \keyw{Friction and wear,Galvanizing,Submerged hardware,Superalloys} + \endentry + \entry{ashworthMicrostructurePropertyRelationships1999}{article}{}{} + \name{author}{3}{}{% + {{hash=a0a9668f5a93080c8425a8cf80e9d0d2}{% + family={Ashworth}, + familyi={A\bibinitperiod}, + given={M.A.}, + giveni={M\bibinitperiod}}}% + {{hash=27753a82b6390957cb920ec5052f0810}{% + family={Jacobs}, + familyi={J\bibinitperiod}, + given={M.H.}, + giveni={M\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \list{language}{1}{% + {EN}% + } + \strng{namehash}{abac9b3a3bd887c0c8dedb4a4e169c92} + \strng{fullhash}{68dce5901af799f73fc399cf947f81b9} + \strng{fullhashraw}{68dce5901af799f73fc399cf947f81b9} + \strng{bibnamehash}{68dce5901af799f73fc399cf947f81b9} + \strng{authorbibnamehash}{68dce5901af799f73fc399cf947f81b9} + \strng{authornamehash}{abac9b3a3bd887c0c8dedb4a4e169c92} + \strng{authorfullhash}{68dce5901af799f73fc399cf947f81b9} + \strng{authorfullhashraw}{68dce5901af799f73fc399cf947f81b9} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{In the present paper the microstructure and properties of a range of hipped Stellite powders are investigated, the basic aim of the study being to generate a materia/property database to facilitate alloy selection for potential applications involving net shape component manufacture. Particular attention is paid to the morphology, particle size distribution, and surface composition of the as atomised powders and their effect on subsequent consolidation. The consolidated powders are fully characterised in terms of microstructure and the composition and distribution of secondary phases. The effect of hipping temperature on the microstructure, hardness, and tensile properties of the powders are discussed in terms of the optimum processing temperature for the various alloys.} + \field{issn}{0032-5899} + \field{journaltitle}{Powder Metallurgy} + \field{month}{3} + \field{note}{23 citations (Semantic Scholar/DOI) [2025-04-12] Publisher: SAGE Publications} + \field{number}{3} + \field{title}{Microstructure and property relationships in hipped {Stellite} powders} + \field{urlday}{3} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{42} + \field{year}{1999} + \field{urldateera}{ce} + \field{pages}{243\bibrangedash 249} + \range{pages}{7} + \verb{doi} + \verb 10.1179/003258999665585 + \endverb + \verb{urlraw} + \verb https://journals.sagepub.com/action/showAbstract + \endverb + \verb{url} + \verb https://journals.sagepub.com/action/showAbstract + \endverb + \endentry + \entry{ferozhkhanMetallurgicalStudyStellite2017}{article}{}{} + \name{author}{3}{}{% + {{hash=bed071d3745587c303d1b4411281a295}{% + family={Ferozhkhan}, + familyi={F\bibinitperiod}, + given={Mohammed\bibnamedelima Mohaideen}, + giveni={M\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=fdb6a42317e0e10a267ce7c918a63e11}{% + family={Kumar}, + familyi={K\bibinitperiod}, + given={Kottaimathan\bibnamedelima Ganesh}, + giveni={K\bibinitperiod\bibinitdelim G\bibinitperiod}}}% + {{hash=250edfbd96cbc7ebd974dd11a2098198}{% + family={Ravibharath}, + familyi={R\bibinitperiod}, + given={Rajanbabu}, + giveni={R\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \strng{namehash}{7a694c7ba4c57888494ddc3675c7d70c} + \strng{fullhash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{fullhashraw}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{bibnamehash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authorbibnamehash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authornamehash}{7a694c7ba4c57888494ddc3675c7d70c} + \strng{authorfullhash}{c63a5ee4b2edf1e71712795226de5b1a} + \strng{authorfullhashraw}{c63a5ee4b2edf1e71712795226de5b1a} + \field{sortinit}{1} + \field{sortinithash}{4f6aaa89bab872aa0999fec09ff8e98a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{309-16L stainless steel was deposited over base metal Grade 91 steel (9Cr–1Mo) as buffer layer by shielded metal arc welding (SMAW), gas tungsten arc welding (GTAW) and flux cored arc welding processes, and then, Stellite 6 (Co–Cr alloy) was coated on stainless steel buffer by SMAW, GTAW and plasma transferred arc welding processes. Stellite 6 coatings were characterized using optical microscope, Vickers hardness tester and optical emission spectrometer, respectively. The FCA deposit has less heat-affected zone and uniform hardness than SMA and GTA deposits. The buffer layer has reduced the formation of any surface cracks and delamination near the fusion zones. The microstructure of Stellite 6 consists of dendrites of Co solid solution and carbides secretion in the interdendrites of Co and Cr matrix. Electron-dispersive spectroscopy line scan has been conducted to analyse the impact of alloying elements in the fusion line and Stellite 6 deposits. It was observed that dilution of Fe in PTA-deposited Stellite 6 was lesser than SMA and GTA deposits and uniform hardness of 600–650 \$\${\textbackslash}hbox \{HV\}\_\{0.3\}\$\$was obtained from PTA deposit. The chemical analysis resulted in alloy composition of PTA deposit has nominal percentage in comparison with consumable composition while GTA and SMA deposits has high dilution of Fe and Ni.} + \field{issn}{2191-4281} + \field{journaltitle}{Arabian Journal for Science and Engineering} + \field{month}{5} + \field{note}{0 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{5} + \field{title}{Metallurgical {Study} of {Stellite} 6 {Cladding} on 309-{16L} {Stainless} {Steel}} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{42} + \field{year}{2017} + \field{urldateera}{ce} + \field{pages}{2067\bibrangedash 2074} + \range{pages}{8} + \verb{doi} + \verb 10.1007/s13369-017-2457-7 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/s13369-017-2457-7 + \endverb + \verb{url} + \verb https://doi.org/10.1007/s13369-017-2457-7 + \endverb + \keyw{Dilution,EDS,Hardfacing,Interdendrites,Stellite} + \endentry + \entry{pacquentinTemperatureInfluenceRepair2025}{article}{}{} + \name{author}{5}{}{% + {{hash=096b7ba62dd31bb3abb4c7daa2ba6477}{% + family={Pacquentin}, + familyi={P\bibinitperiod}, + given={Wilfried}, + giveni={W\bibinitperiod}}}% + {{hash=9e420ee86aa957c365d57085e999996c}{% + family={Wident}, + familyi={W\bibinitperiod}, + given={Pierre}, + giveni={P\bibinitperiod}}}% + {{hash=268ededdba463184d10a8f5532d5cf81}{% + family={Varlet}, + familyi={V\bibinitperiod}, + given={Jérôme}, + giveni={J\bibinitperiod}}}% + {{hash=b24f3669f2a577f8062abf9d04e0e179}{% + family={Cailloux}, + familyi={C\bibinitperiod}, + given={Thomas}, + giveni={T\bibinitperiod}}}% + {{hash=ba3f789128096170532622dc53c3bbd0}{% + family={Maskrot}, + familyi={M\bibinitperiod}, + given={Hicham}, + giveni={H\bibinitperiod}}}% + } + \strng{namehash}{f57606f1b71f32267dc7727ee385b008} + \strng{fullhash}{0cc41d1605707534d43f79ae97691cbc} + \strng{fullhashraw}{0cc41d1605707534d43f79ae97691cbc} + \strng{bibnamehash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authorbibnamehash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authornamehash}{f57606f1b71f32267dc7727ee385b008} + \strng{authorfullhash}{0cc41d1605707534d43f79ae97691cbc} + \strng{authorfullhashraw}{0cc41d1605707534d43f79ae97691cbc} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Additive manufacturing (AM) is a proven time- and cost-effective method for repairing parts locally damaged after e.g. repetitive friction wear or corrosion. Repairing a hardfacing coating using AM technologies presents however several simultaneous challenges arising from the complex geometry and a high probability of crack formation due to process-induced stress. We address the repair of a cobalt-based Stellite™ 6 hardfacing coating on an AISI 316L substrate performed using Laser Powder Directed Energy Deposition (LP-DED) and investigate the influence of key process features and parameters. We describe our process which successfully prevents crack formation both during and after the repair, highlighting the design of the preliminary part machining phase, induction heating of an extended part volume during the laser repair phase and the optimal scanning strategy. Local characterization using non-destructive testing, Vickers hardness measurements and microstructural examinations by scanning electron microscopy (SEM) show an excellent metallurgical quality of the repair and its interface with the original part. In addition, we introduce an innovative process qualification test assessing the repair quality and innocuity, which is based on the global response to induced cracks and probes the absence of crack attraction by the repair (ACAR11ACAR stands for absence of crack attraction by the repair.). Here this ACAR test reveals a slight difference in mechanical behavior between the repair and the original coating which motivates further work to eventually make the repair imperceptible.} + \field{issn}{2666-3309} + \field{journaltitle}{Journal of Advanced Joining Processes} + \field{month}{6} + \field{title}{Temperature influence on the repair of a hardfacing coating using laser metal deposition and assessment of the repair innocuity} + \field{urlday}{31} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{11} + \field{year}{2025} + \field{urldateera}{ce} + \field{pages}{100284} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.jajp.2025.100284 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S2666330925000056 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S2666330925000056 + \endverb + \keyw{Additive manufacturing,Direct laser deposition,Hardfacing coating,Mechanical characterization,Repair,Repair innocuity assessment} + \endentry + \entry{desaiEffectCarbideSize1984}{article}{}{} + \name{author}{4}{}{% + {{hash=fc05df304d9bc11398a5c124af37591d}{% + family={Desai}, + familyi={D\bibinitperiod}, + given={V.\bibnamedelimi M.}, + giveni={V\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=ec550afc1e3aea4900fb58655a64f6da}{% + family={Rao}, + familyi={R\bibinitperiod}, + given={C.\bibnamedelimi M.}, + giveni={C\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=33b6be2f67c7c521e0d9dd2e94cb03fa}{% + family={Kosel}, + familyi={K\bibinitperiod}, + given={T.\bibnamedelimi H.}, + giveni={T\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + {{hash=1ad7f5a75d8dc26e538ca7e4d233e622}{% + family={Fiore}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi F.}, + giveni={N\bibinitperiod\bibinitdelim F\bibinitperiod}}}% + } + \strng{namehash}{aeae2b334e415789011cf05b2beda57d} + \strng{fullhash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{fullhashraw}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{bibnamehash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authorbibnamehash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authornamehash}{aeae2b334e415789011cf05b2beda57d} + \strng{authorfullhash}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \strng{authorfullhashraw}{3e12109fb3ad3bbc6eba6a83ee61b7de} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{A study of the effect of carbide size on the abrasion resistance of two cobalt-base powder metallurgy alloys, alloys 6 and 19, was conducted using low stress abrasion with a relatively hard abrasive, A12O3. Specimens of each alloy were produced with different carbide sizes but with a constant carbide volume fraction. The wear test results show a monotonie decrease in wear rate with increasing carbide size. Scanning electron microscopy of the worn surfaces and of wear debris particles shows that the primary material removal mechanism is micromachining. Small carbides provide little resistance to micromachining because of the fact that many of them are contained entirely in the volume of micromachining chips. The large carbides must be directly cut by the abrasive particles. Other less frequently observed material removal mechanisms included direct carbide pull-out and the formation of large pits in fine carbide specimens. These processes are considered secondary in the present work, but they may have greater importance in wear by relatively soft abrasives which do not cut chips from the carbide phase of these alloys. Some indication of this is provided by limited studies using a relatively soft abrasive, rounded quartz.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{59 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{title}{Effect of carbide size on the abrasion of cobalt-base powder metallurgy alloys} + \field{urlday}{17} + \field{urlmonth}{11} + \field{urlyear}{2024} + \field{volume}{94} + \field{year}{1984} + \field{urldateera}{ce} + \field{pages}{89\bibrangedash 101} + \range{pages}{13} + \verb{doi} + \verb 10.1016/0043-1648(84)90168-6 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/0043164884901686 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/0043164884901686 + \endverb + \keyw{Cavitation,Cavitation equipment,Damage measurement,Instrumentation,Sodium} + \endentry + \entry{francCavitationErosion2005}{incollection}{}{} + \name{editor}{2}{}{% + {{hash=82466166f53e07ad9568dba9555563e7}{% + family={Franc}, + familyi={F\bibinitperiod}, + given={Jean-Pierre}, + giveni={J\bibinithyphendelim P\bibinitperiod}}}% + {{hash=441eced1863753c712f0eaa788cbc3d5}{% + family={Michel}, + familyi={M\bibinitperiod}, + given={Jean-Marie}, + giveni={J\bibinithyphendelim M\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \list{location}{1}{% + {Dordrecht}% + } + \list{publisher}{1}{% + {Springer Netherlands}% + } + \strng{namehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{fullhash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{fullhashraw}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{bibnamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorbibnamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editornamehash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorfullhash}{9ef3cd89643a1a5e288c68eb93b9390c} + \strng{editorfullhashraw}{9ef3cd89643a1a5e288c68eb93b9390c} + \field{sortinit}{4} + \field{sortinithash}{9381316451d1b9788675a07e972a12a7} + \field{labelnamesource}{editor} + \field{labeltitlesource}{title} + \field{booktitle}{Fundamentals of {Cavitation}} + \field{isbn}{978-1-4020-2233-3} + \field{title}{Cavitation {Erosion}} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{year}{2005} + \field{urldateera}{ce} + \field{pages}{265\bibrangedash 291} + \range{pages}{27} + \verb{doi} + \verb 10.1007/1-4020-2233-6_12 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/1-4020-2233-6_12 + \endverb + \verb{url} + \verb https://doi.org/10.1007/1-4020-2233-6_12 + \endverb + \keyw{Acoustic Impedance,Adverse Pressure Gradient,Mass Loss Rate,Pressure Pulse,Solid Wall} + \endentry + \entry{romoCavitationHighvelocitySlurry2012}{article}{}{} + \name{author}{4}{}{% + {{hash=abd07783347fdc165942b01479e16afb}{% + family={Romo}, + familyi={R\bibinitperiod}, + given={S.A.}, + giveni={S\bibinitperiod}}}% + {{hash=9c9837ed5fce5c7a1aeb233aa99aa04d}{% + family={Santa}, + familyi={S\bibinitperiod}, + given={J.F.}, + giveni={J\bibinitperiod}}}% + {{hash=fecaae68172b53756247ca68af700ed9}{% + family={Giraldo}, + familyi={G\bibinitperiod}, + given={J.E.}, + giveni={J\bibinitperiod}}}% + {{hash=467faf266d1206e4566fe6d0465b33f0}{% + family={Toro}, + familyi={T\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{285bcf9d2b83436d537b5e21b7fde046} + \strng{fullhash}{e0312588d226589c879f5d182ca350e9} + \strng{fullhashraw}{e0312588d226589c879f5d182ca350e9} + \strng{bibnamehash}{e0312588d226589c879f5d182ca350e9} + \strng{authorbibnamehash}{e0312588d226589c879f5d182ca350e9} + \strng{authornamehash}{285bcf9d2b83436d537b5e21b7fde046} + \strng{authorfullhash}{e0312588d226589c879f5d182ca350e9} + \strng{authorfullhashraw}{e0312588d226589c879f5d182ca350e9} + \field{sortinit}{4} + \field{sortinithash}{9381316451d1b9788675a07e972a12a7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The cavitation and slurry erosion resistances of Stellite 6 coatings and 13-4 stainless steel were compared in laboratory. The Cavitation Resistance (CR) was measured according to ASTM G32 standard and the Slurry Erosion Resistance (SER) was tested in a high-velocity erosion tester under several impact angles. The results showed that the coatings improved the CR 15 times when compared to bare stainless steel. The SER of the coatings was also higher for all the impingement angles tested, the highest erosion rate being observed at 45°. The main wear mechanisms were micro-cracking (cavitation tests), and micro-cutting and micro-ploughing (slurry erosion tests). © 2011 Elsevier Ltd. All rights reserved.} + \field{issn}{0301679X (ISSN)} + \field{journaltitle}{Tribology International} + \field{note}{82 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Cavitation and high-velocity slurry erosion resistance of welded {Stellite} 6 alloy} + \field{volume}{47} + \field{year}{2012} + \field{pages}{16\bibrangedash 24} + \range{pages}{9} + \verb{doi} + \verb 10.1016/j.triboint.2011.10.003 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-84856240362&doi=10.1016%2fj.triboint.2011.10.003&partnerID=40&md5=77bc5b529937543083c683cc6f5d689d + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-84856240362&doi=10.1016%2fj.triboint.2011.10.003&partnerID=40&md5=77bc5b529937543083c683cc6f5d689d + \endverb + \keyw{Cavitation,Cavitation corrosion,Cavitation erosion,Cavitation resistance,Cerium alloys,Chromate coatings,Erosion,Erosion rates,High velocity,Impact angles,Impact resistance,Impingement angle,Micro-cutting,Slurry erosion,Stainless steel,Stellite,Stellite 6,Stellite 6 alloy,Stellite 6 coating,Tribology,Wear mechanisms,alloy} + \endentry + \entry{gevariDirectIndirectThermal2020}{article}{}{} + \name{author}{5}{}{% + {{hash=93d9cff817608f96c206941face4c5d7}{% + family={Gevari}, + familyi={G\bibinitperiod}, + given={Moein\bibnamedelima Talebian}, + giveni={M\bibinitperiod\bibinitdelim T\bibinitperiod}}}% + {{hash=e271948379fd6fee4bd30a4d576761b8}{% + family={Abbasiasl}, + familyi={A\bibinitperiod}, + given={Taher}, + giveni={T\bibinitperiod}}}% + {{hash=67d0558f57dbf7548b5b43a80b85f47f}{% + family={Niazi}, + familyi={N\bibinitperiod}, + given={Soroush}, + giveni={S\bibinitperiod}}}% + {{hash=efb87c095e41c6349ba97d939982e130}{% + family={Ghorbani}, + familyi={G\bibinitperiod}, + given={Morteza}, + giveni={M\bibinitperiod}}}% + {{hash=311cf929c32c6c2ce5aa2728ae09ad47}{% + family={Koşar}, + familyi={K\bibinitperiod}, + given={Ali}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{76843143b68c90c6ac5d9d854fd56c1f} + \strng{fullhash}{7e654139b427bf36f3a25a5848105f5b} + \strng{fullhashraw}{7e654139b427bf36f3a25a5848105f5b} + \strng{bibnamehash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authorbibnamehash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authornamehash}{76843143b68c90c6ac5d9d854fd56c1f} + \strng{authorfullhash}{7e654139b427bf36f3a25a5848105f5b} + \strng{authorfullhashraw}{7e654139b427bf36f3a25a5848105f5b} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{shorttitle} + \field{abstract}{The phase change phenomenon in fluids as a result of low local pressure under a critical value is known as cavitation. Acoustic wave propagation or hydrodynamic pressure drop of the working fluid are the main reasons for inception of this phenomenon. Considering the released energy from the collapsing cavitation bubbles as a reliable source has led to its implementation to different fields, namely, heat transfer, surface cleaning and fouling, water treatment, food industry, chemical reactions, energy harvesting. A considerable amount of energy in the mentioned industries is required for thermal applications. Cavitation could serve for minimizing the energy demand and optimizing the processes. Thus, the energy efficiency of the systems could be significantly enhanced. This review article focuses on the direct and indirect thermal applications of hydrodynamic and acoustic cavitation. Relevant studies with emerging applications are discussed, while developments in cavitation, which have given rise to thermal applications during the last decade, are also included in this review.} + \field{issn}{1359-4311} + \field{journaltitle}{Applied Thermal Engineering} + \field{month}{5} + \field{note}{84 citations (Semantic Scholar/DOI) [2025-04-13]} + \field{shorttitle}{Direct and indirect thermal applications of hydrodynamic and acoustic cavitation} + \field{title}{Direct and indirect thermal applications of hydrodynamic and acoustic cavitation: {A} review} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{171} + \field{year}{2020} + \field{urldateera}{ce} + \field{pages}{115065} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.applthermaleng.2020.115065 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S135943111937766X + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S135943111937766X + \endverb + \keyw{Acoustic cavitation,Food industry,Heat transfer enhancement,Hydrodynamic cavitation,Water treatment} + \endentry + \entry{shinEffectMolybdenumMicrostructure2003}{article}{}{} + \name{author}{5}{}{% + {{hash=11c1c63fde4778e27fd93d2389dd1d9f}{% + family={Shin}, + familyi={S\bibinitperiod}, + given={Jong-Choul}, + giveni={J\bibinithyphendelim C\bibinitperiod}}}% + {{hash=4d7d3c5a5d25916fcbdacaec6e7b281c}{% + family={Doh}, + familyi={D\bibinitperiod}, + given={Jung-Man}, + giveni={J\bibinithyphendelim M\bibinitperiod}}}% + {{hash=9257782113324f27de8d34043cd84f7b}{% + family={Yoon}, + familyi={Y\bibinitperiod}, + given={Jin-Kook}, + giveni={J\bibinithyphendelim K\bibinitperiod}}}% + {{hash=f1733c8d49f956fedeb6a8c03ce455c9}{% + family={Lee}, + familyi={L\bibinitperiod}, + given={Dok-Yol}, + giveni={D\bibinithyphendelim Y\bibinitperiod}}}% + {{hash=d2534382552f3c10ee00cd39f0979de1}{% + family={Kim}, + familyi={K\bibinitperiod}, + given={Jae-Soo}, + giveni={J\bibinithyphendelim S\bibinitperiod}}}% + } + \strng{namehash}{35defe2b8f7d338cdec33698baeff00a} + \strng{fullhash}{178cbc46d086767ebf3c6301cad009cf} + \strng{fullhashraw}{178cbc46d086767ebf3c6301cad009cf} + \strng{bibnamehash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authorbibnamehash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authornamehash}{35defe2b8f7d338cdec33698baeff00a} + \strng{authorfullhash}{178cbc46d086767ebf3c6301cad009cf} + \strng{authorfullhashraw}{178cbc46d086767ebf3c6301cad009cf} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The Stellite 6 hardfacing alloys with different Mo contents have been deposited on AISI 1045-carbon steel using a Plasma Transferred Arc (PTA) welding machine. The effect of Mo on the microstructures and wear resistance properties of the Stellite 6 hardfacing alloys were investigated using optical microscopy, scanning electron microscopy, electron probe microanalysis and X-ray diffraction. With an increase in Mo contents, the M23C6 and M6C type carbides were formed instead of Cr-rich M7C3 and M23C6 type carbides observed in the interdenritic region of the Mo-free Stellite 6 hardfacing alloy. The size of Cr-rich carbides in interdendritic region decreased, but that of M6C type carbide increased as well as the refinement of Co-rich dendrites. The volume fraction of Cr-rich carbides slightly increased, but that of M6C type carbide abruptly increased. This microstructural change was responsible for the improvement of the mechanical properties such as hardness and wear resistance of the Mo-modified Stellite 6 hardfacing alloy.} + \field{issn}{0257-8972} + \field{journaltitle}{Surface and Coatings Technology} + \field{month}{3} + \field{number}{2} + \field{title}{Effect of molybdenum on the microstructure and wear resistance of cobalt-base {Stellite} hardfacing alloys} + \field{urlday}{5} + \field{urlmonth}{3} + \field{urlyear}{2025} + \field{volume}{166} + \field{year}{2003} + \field{urldateera}{ce} + \field{pages}{117\bibrangedash 126} + \range{pages}{10} + \verb{doi} + \verb 10.1016/S0257-8972(02)00853-8 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0257897202008538 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0257897202008538 + \endverb + \keyw{Co-base Stellite alloys,Microstructure and wear resistance,Molybdenum,PTA} + \endentry + \entry{ahmedSlidingWearBlended2021a}{article}{}{} + \name{author}{3}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{652318761812c14e2605b641664892df} + \strng{fullhashraw}{652318761812c14e2605b641664892df} + \strng{bibnamehash}{652318761812c14e2605b641664892df} + \strng{authorbibnamehash}{652318761812c14e2605b641664892df} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{652318761812c14e2605b641664892df} + \strng{authorfullhashraw}{652318761812c14e2605b641664892df} + \field{extraname}{3} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This investigation reports on the tribomechanical evaluations of a Co-based alloy obtained by the hot isostatic pressing (HIPing) of a blend of two standard gas atomized cobalt alloy powders. A HIPed blend of Stellite 6 and Stellite 20 was used to investigate the effect of varying the C, Cr, and W content simultaneously on the structure-property relationships. Microstructural evaluations involved scanning electron microscopy and x-ray diffraction. Experimental evaluations were conducted using hardness, impact, tensile, abrasive wear and sliding wear tests to develop an understanding of the mechanical and tribological performance of the alloys. Results are discussed in terms of the failure modes for the mechanical tests, and wear mechanisms for the tribological tests. This study indicates that powder blends can be used to design for a desired combination of mechanical strength and wear properties in these HIPed alloys. Specific relationships were observed between the alloy composition and carbide content, hardness, impact energy and wear resistance. There was a linear relationship between the weighted W- and C-content and the carbide fraction. The abrasive wear performance also showed a linear relationship with the weighted alloy composition. The pin-on-disc and ball-on-flat experiments revealed a more complex relationship between the alloy composition and the wear rate.} + \field{issn}{0043-1648} + \field{journaltitle}{Wear} + \field{month}{2} + \field{note}{18 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Sliding wear of blended cobalt based alloys} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{466-467} + \field{year}{2021} + \field{urldateera}{ce} + \field{pages}{203533} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.wear.2020.203533 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0043164820309923 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0043164820309923 + \endverb + \keyw{Blending,HIPing,Hardness,Powder metallurgy,Sliding wear,Stellite alloy} + \endentry + \entry{crookCobaltbaseAlloysResist1994}{article}{}{} + \name{author}{1}{}{% + {{hash=16985215fbfc4124567154cd4ca61487}{% + family={Crook}, + familyi={C\bibinitperiod}, + given={P}, + giveni={P\bibinitperiod}}}% + } + \strng{namehash}{16985215fbfc4124567154cd4ca61487} + \strng{fullhash}{16985215fbfc4124567154cd4ca61487} + \strng{fullhashraw}{16985215fbfc4124567154cd4ca61487} + \strng{bibnamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authorbibnamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authornamehash}{16985215fbfc4124567154cd4ca61487} + \strng{authorfullhash}{16985215fbfc4124567154cd4ca61487} + \strng{authorfullhashraw}{16985215fbfc4124567154cd4ca61487} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{issn}{0882-7958} + \field{journaltitle}{Cobalt-base alloys resist wear, corrosion, and heat} + \field{note}{Place: Materials Park, OH Publisher: ASM International} + \field{number}{4} + \field{title}{Cobalt-base alloys resist wear, corrosion, and heat} + \field{volume}{145} + \field{year}{1994} + \field{pages}{27\bibrangedash 30} + \range{pages}{4} + \endentry + \entry{huangMicrostructureEvolutionMartensite2023}{article}{}{} + \name{author}{6}{}{% + {{hash=55328195d8b2c0f90f11e12f5ddb7d65}{% + family={Huang}, + familyi={H\bibinitperiod}, + given={Zonglian}, + giveni={Z\bibinitperiod}}}% + {{hash=2938deb5048323c6e1bfdd80975d5b28}{% + family={Wang}, + familyi={W\bibinitperiod}, + given={Bo}, + giveni={B\bibinitperiod}}}% + {{hash=0138deaf332692ced30d823b9cebc488}{% + family={Liu}, + familyi={L\bibinitperiod}, + given={Fei}, + giveni={F\bibinitperiod}}}% + {{hash=92c4cc87ddf9f0a5abb5ff8d5b8878d4}{% + family={Song}, + familyi={S\bibinitperiod}, + given={Min}, + giveni={M\bibinitperiod}}}% + {{hash=971be18e8809118d44c885580820c916}{% + family={Ni}, + familyi={N\bibinitperiod}, + given={Song}, + giveni={S\bibinitperiod}}}% + {{hash=eb96d2754cddae273dd482f087734e31}{% + family={Liu}, + familyi={L\bibinitperiod}, + given={Shaojun}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{61779e4ce456f415f5dc118db21bed83} + \strng{fullhash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{fullhashraw}{8ca9ebea09cf1f645c339306001d45ac} + \strng{bibnamehash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authorbibnamehash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authornamehash}{61779e4ce456f415f5dc118db21bed83} + \strng{authorfullhash}{8ca9ebea09cf1f645c339306001d45ac} + \strng{authorfullhashraw}{8ca9ebea09cf1f645c339306001d45ac} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{The influence of laser energy density and heat treatment on the microstructure and properties of Co-Cr-Mo-W alloys fabricated by selective laser melting (SLM) are investigated symmetrically. When the laser power, the scanning speed, and the scanning space are set as 160 W, 400 mm/s, and 0.07 mm, respectively, the SLM-ed Co-Cr-Mo-W alloys display high strength and good ductility simultaneously. The precipitates ranging from nano- to macro- scale are finely distributed in SLM-ed CoCr alloys grains and/or along the grain boundaries in the heat treated alloys. Co-Cr-Mo-W alloys with an excellent combination of strength and ductility can be achieved by tailoring the microstructure and morphology of SLM-ed alloys during the heat treatment. The tensile strength, yield strength, and elongation are 1221.38 ± 10 MPa, 778.81 ± 12 MPa, and 17.2 ± 0.67\%, respectively.} + \field{issn}{0263-4368} + \field{journaltitle}{International Journal of Refractory Metals and Hard Materials} + \field{month}{6} + \field{title}{Microstructure evolution, martensite transformation and mechanical properties of heat treated {Co}-{Cr}-{Mo}-{W} alloys by selective laser melting} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{113} + \field{year}{2023} + \field{urldateera}{ce} + \field{pages}{106170} + \range{pages}{1} + \verb{doi} + \verb 10.1016/j.ijrmhm.2023.106170 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0263436823000707 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0263436823000707 + \endverb + \keyw{Co–Cr–Mo-W alloys,Heat treatment,Martensite phase transformation,Mechanical properties,Selective laser melting} + \endentry + \entry{tawancyFccHcpTransformation1986}{article}{}{} + \name{author}{3}{}{% + {{hash=f3547527506994c69c774b2c0d77ac73}{% + family={Tawancy}, + familyi={T\bibinitperiod}, + given={H.\bibnamedelimi M.}, + giveni={H\bibinitperiod\bibinitdelim M\bibinitperiod}}}% + {{hash=f7d566a34064f3d0ccab33dde7a34069}{% + family={Ishwar}, + familyi={I\bibinitperiod}, + given={V.\bibnamedelimi R.}, + giveni={V\bibinitperiod\bibinitdelim R\bibinitperiod}}}% + {{hash=6f964da88776c95344b60d3d9b6241fa}{% + family={Lewis}, + familyi={L\bibinitperiod}, + given={B.\bibnamedelimi E.}, + giveni={B\bibinitperiod\bibinitdelim E\bibinitperiod}}}% + } + \list{language}{1}{% + {en}% + } + \strng{namehash}{4de94c11cde2eac1de960723e9eac321} + \strng{fullhash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{fullhashraw}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{bibnamehash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authorbibnamehash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authornamehash}{4de94c11cde2eac1de960723e9eac321} + \strng{authorfullhash}{b41586e8f4d7f9d36d48a78941a8c3b5} + \strng{authorfullhashraw}{b41586e8f4d7f9d36d48a78941a8c3b5} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{issn}{1573-4811} + \field{journaltitle}{Journal of Materials Science Letters} + \field{month}{3} + \field{note}{33 citations (Semantic Scholar/DOI) [2025-04-13]} + \field{number}{3} + \field{title}{On the fcc → hcp transformation in a cobalt-base superalloy ({Haynes} alloy {No}. 25)} + \field{urlday}{13} + \field{urlmonth}{4} + \field{urlyear}{2025} + \field{volume}{5} + \field{year}{1986} + \field{urldateera}{ce} + \field{pages}{337\bibrangedash 341} + \range{pages}{5} + \verb{doi} + \verb 10.1007/BF01748098 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1007/BF01748098 + \endverb + \verb{url} + \verb https://doi.org/10.1007/BF01748098 + \endverb + \keyw{Haynes Alloy,Polymer,Polymers} + \endentry + \entry{yuComparisonTriboMechanicalProperties2007}{article}{}{} + \name{author}{3}{}{% + {{hash=f46cff6a47143fdbd36ae8842919e073}{% + family={Yu}, + familyi={Y\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=39fbce992265c4dd42ff7cb6ab804ded}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + } + \strng{namehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{fullhash}{8e67a0a25c7114030e7e739ed034990b} + \strng{fullhashraw}{8e67a0a25c7114030e7e739ed034990b} + \strng{bibnamehash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authorbibnamehash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authornamehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{authorfullhash}{8e67a0a25c7114030e7e739ed034990b} + \strng{authorfullhashraw}{8e67a0a25c7114030e7e739ed034990b} + \field{extraname}{1} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{This paper aims to compare the tribo-mechanical properties and structure–property relationships of a wear resistant cobalt-based alloy produced via two different manufacturing routes, namely sand casting and powder consolidation by hot isostatic pressing (HIPing). The alloy had a nominal wt \% composition of Co–33Cr–17.5W–2.5C, which is similar to the composition of commercially available Stellite 20 alloy. The high tungsten and carbon contents provide resistance to severe abrasive and sliding wear. However, the coarse carbide structure of the cast alloy also gives rise to brittleness. Hence this research was conducted to comprehend if the carbide refinement and corresponding changes in the microstructure, caused by changing the processing route to HIPing, could provide additional merits in the tribo-mechanical performance of this alloy. The HIPed alloy possessed a much finer microstructure than the cast alloy. Both alloys had similar hardness, but the impact resistance of the HIPed alloy was an order of magnitude higher than the cast counterpart. Despite similar abrasive and sliding wear resistance of both alloys, their main wear mechanisms were different due to their different carbide morphologies. Brittle fracture of the carbides and ploughing of the matrix were the main wear mechanisms for the cast alloy, whereas ploughing and carbide pullout were the dominant wear mechanisms for the HIPed alloy. The HIPed alloy showed significant improvement in contact fatigue performance, indicating its superior impact and fatigue resistance without compromising the hardness and sliding∕abrasive wear resistance, which makes it suitable for relatively higher stress applications.} + \field{issn}{0742-4787} + \field{journaltitle}{Journal of Tribology} + \field{month}{1} + \field{note}{37 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{3} + \field{title}{A {Comparison} of the {Tribo}-{Mechanical} {Properties} of a {Wear} {Resistant} {Cobalt}-{Based} {Alloy} {Produced} by {Different} {Manufacturing} {Processes}} + \field{urlday}{17} + \field{urlmonth}{11} + \field{urlyear}{2024} + \field{volume}{129} + \field{year}{2007} + \field{urldateera}{ce} + \field{pages}{586\bibrangedash 594} + \range{pages}{9} + \verb{doi} + \verb 10.1115/1.2736450 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1115/1.2736450 + \endverb + \verb{url} + \verb https://doi.org/10.1115/1.2736450 + \endverb + \endentry + \entry{stoicaInfluenceHeattreatmentSliding2005}{article}{}{} + \name{author}{3}{}{% + {{hash=9ee308ed1264406c99dc3dc19fc74bbc}{% + family={Stoica}, + familyi={S\bibinitperiod}, + given={V.}, + giveni={V\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=396db0229b4cd75917372e6b8a4c12ee}{% + family={Itsukaichi}, + familyi={I\bibinitperiod}, + given={T.}, + giveni={T\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{1dad3e925506f0bfcbc611fb083a4a04} + \strng{fullhash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{fullhashraw}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{bibnamehash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authorbibnamehash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authornamehash}{1dad3e925506f0bfcbc611fb083a4a04} + \strng{authorfullhash}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \strng{authorfullhashraw}{09c4b7a69ffaf05661ccd1c9f30d41c3} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Functionally graded WC-NiCrBSi coatings were thermally sprayed using a High Velocity Oxy-Fuel (JP5000) system and heat-treated at 1200 °C in argon environment. The relative performance of the as-sprayed and heat-treated coatings was investigated in sliding wear under different tribological conditions of contact stress, and test couple configuration, using a high frequency reciprocating ball on plate rig. Test results are discussed with the help of microstructural evaluations and mechanical properties measurements. Results indicate that by heat-treating the coatings at a temperature of 1200 °C, it is possible to achieve higher wear resistance, both in terms of coating wear, as well as the total wear of the test couples. This was attributed to the improvements in the coating microstructure during the heat-treatment, which resulted in an improvement in coating's mechanical properties through the formation of hard phases, elimination of brittle W2C and W, and the establishment of metallurgical bonding within the coating microstructure. © 2005 Elsevier B.V. All rights reserved.} + \field{issn}{02578972 (ISSN)} + \field{journaltitle}{Surface and Coatings Technology} + \field{note}{41 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{1} + \field{title}{Influence of heat-treatment on the sliding wear of thermal spray cermet coatings} + \field{volume}{199} + \field{year}{2005} + \field{pages}{7\bibrangedash 21} + \range{pages}{15} + \verb{doi} + \verb 10.1016/j.surfcoat.2005.03.026 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-21844464044&doi=10.1016%2fj.surfcoat.2005.03.026&partnerID=40&md5=6ad736723e828d39edf4a37c5975d2dc + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-21844464044&doi=10.1016%2fj.surfcoat.2005.03.026&partnerID=40&md5=6ad736723e828d39edf4a37c5975d2dc + \endverb + \keyw{Bonding,Brittleness,Cermets,Coating microstructure,Frequencies,Functionally graded materials,Heat treatment,Heat-treated coatings,Heat-treatment,High Velocity Oxy-Fuel,Mechanical properties,Microstructure,Nickel compounds,Phase composition,Sliding wear,Sprayed coatings,Thermal spray coatings,Tribology,Tungsten compounds,Wear of materials,heat treatment,sliding wear} + \endentry + \entry{ahmedInfluenceReHIPingStructure2013}{article}{}{} + \name{author}{4}{}{% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=75bf7913ab7463c6e3734bec975046fc}{% + family={Villiers\bibnamedelima Lovelock}, + familyi={V\bibinitperiod\bibinitdelim L\bibinitperiod}, + given={H.\bibnamedelimi L.}, + giveni={H\bibinitperiod\bibinitdelim L\bibinitperiod}, + prefix={de}, + prefixi={d\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + {{hash=1c8f35a67217a8f6cbd1f8d3edb797b0}{% + family={Faisal}, + familyi={F\bibinitperiod}, + given={N.\bibnamedelimi H.}, + giveni={N\bibinitperiod\bibinitdelim H\bibinitperiod}}}% + } + \strng{namehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{fullhash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{fullhashraw}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{bibnamehash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authorbibnamehash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authornamehash}{82fc6b0dd69b51d07006a5e8127c7a8f} + \strng{authorfullhash}{e70fdd408b4a5e9730bd0722565b8e34} + \strng{authorfullhashraw}{e70fdd408b4a5e9730bd0722565b8e34} + \field{extraname}{4} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{HIP-consolidation (Hot Isostatic Pressing or HIPing) of cobalt-based Stellite alloys offers significant technological advantages for components operating in aggressive wear environments. The aim of this investigation was to ascertain the effect of re-HIPing on the HIPed alloy properties for Stellite 4, 6 and 20 alloys. Structure–property relationships are discussed on the basis of microstructural and tribo-mechanical evaluations. Re-HIPing results in coarsening of carbides and solid solution strengthening of the matrix. The average indentation modulus improved, as did the average hardness at micro- and nano-scales. Re-HIPing showed improvement in wear properties the extent of which was dependent on alloy composition.} + \field{issn}{0301-679X} + \field{journaltitle}{Tribology International} + \field{month}{1} + \field{note}{38 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{title}{Influence of {Re}-{HIPing} on the structure–property relationships of cobalt-based alloys} + \field{urlday}{30} + \field{urlmonth}{6} + \field{urlyear}{2024} + \field{volume}{57} + \field{year}{2013} + \field{urldateera}{ce} + \field{pages}{8\bibrangedash 21} + \range{pages}{14} + \verb{doi} + \verb 10.1016/j.triboint.2012.06.025 + \endverb + \verb{urlraw} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X12002241 + \endverb + \verb{url} + \verb https://www.sciencedirect.com/science/article/pii/S0301679X12002241 + \endverb + \keyw{Abrasive wear,Cobalt based alloys,HIPing and Re-HIPing,Stellite 4,6,20,alloys} + \endentry + \entry{yuInfluenceManufacturingProcess2008}{article}{}{} + \name{author}{4}{}{% + {{hash=f46cff6a47143fdbd36ae8842919e073}{% + family={Yu}, + familyi={Y\bibinitperiod}, + given={H.}, + giveni={H\bibinitperiod}}}% + {{hash=73be20d7f1a5cbb337df0ca58a8fa420}{% + family={Ahmed}, + familyi={A\bibinitperiod}, + given={R.}, + giveni={R\bibinitperiod}}}% + {{hash=720a4573d41f2302c51d8dfc20eb7025}{% + family={Lovelock}, + familyi={L\bibinitperiod}, + given={H.\bibnamedelimi de\bibnamedelima Villiers}, + giveni={H\bibinitperiod\bibinitdelim d\bibinitperiod\bibinitdelim V\bibinitperiod}}}% + {{hash=0e68382b25995f7a55c9b600def7c365}{% + family={Davies}, + familyi={D\bibinitperiod}, + given={S.}, + giveni={S\bibinitperiod}}}% + } + \strng{namehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{fullhash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{fullhashraw}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{bibnamehash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authorbibnamehash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authornamehash}{56581c67a86bce08f334a1ace4c9fccb} + \strng{authorfullhash}{57ca415fdcbe0d531a76658a78b7a3d4} + \strng{authorfullhashraw}{57ca415fdcbe0d531a76658a78b7a3d4} + \field{extraname}{2} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{Manufacturing process routes of materials can be adapted to manipulate their microstructure and hence their tribological performance. As industrial demands push the applications of tribological materials to harsher environments of higher stress, starved lubrication, and improved life performance, manufacturing processes can be tailored to optimize their use in particular engineering applications. The aim of this paper was therefore to comprehend the structure-property relationships of a wear resistant cobalt-based alloy (Stellite 6) produced from two different processing routes of powder consolidated hot isostatic pressing (HIPing) and casting. This alloy had a nominal wt \% composition of Co–28Cr–4.5W–1C, which is commonly used in wear related applications in harsh tribological environments. However, the coarse carbide structure of the cast alloy results in higher brittleness and lower toughness. Hence this research was conducted to comprehend if carbide refinement, caused by changing the processing route to HIPing, could improve the tribomechanical performance of this alloy. Microstructural and tribomechanical evaluations, which involved hardness, impact toughness, abrasive wear, sliding wear, and contact fatigue performance tests, indicated that despite the similar abrasive and sliding wear resistance of both alloys, the HIPed alloy exhibited an improved contact fatigue and impact toughness performance in comparison to the cast counterpart. This difference in behavior is discussed in terms of the structure-property relationships. Results of this research indicated that the HIPing process could provide additional impact and fatigue resistance to this alloy without compromising the hardness and the abrasive/sliding wear resistance, which makes the HIPed alloy suitable for relatively higher stress applications. Results are also compared with a previously reported investigation of the Stellite 20 alloy, which had a much higher carbide content in comparison to the Stellite 6 alloy, caused by the variation in the content of alloying elements. These results indicated that the fatigue resistance did not follow the expected trend of the improvement in impact toughness. In terms of the design process, the combination of hardness, toughness, and carbide content show a complex interdependency, where a 40\% reduction in the average hardness and 60\% reduction in carbide content had a more dominating effect on the contact fatigue resistance when compared with an order of magnitude improvement in the impact toughness of the HIPed Stellite 6 alloy.} + \field{issn}{0742-4787} + \field{journaltitle}{Journal of Tribology} + \field{month}{12} + \field{note}{46 citations (Semantic Scholar/DOI) [2025-04-12]} + \field{number}{011601} + \field{title}{Influence of {Manufacturing} {Process} and {Alloying} {Element} {Content} on the {Tribomechanical} {Properties} of {Cobalt}-{Based} {Alloys}} + \field{urlday}{13} + \field{urlmonth}{7} + \field{urlyear}{2024} + \field{volume}{131} + \field{year}{2008} + \field{urldateera}{ce} + \verb{doi} + \verb 10.1115/1.2991122 + \endverb + \verb{urlraw} + \verb https://doi.org/10.1115/1.2991122 + \endverb + \verb{url} + \verb https://doi.org/10.1115/1.2991122 + \endverb + \endentry + \entry{szalaEffectNitrogenIon2021}{article}{}{} + \name{author}{6}{}{% + {{hash=26ecda2187f0e2b702a2497a5dc3f27d}{% + family={Szala}, + familyi={S\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + {{hash=b1f8638f62fc396f39212102aa9a7be4}{% + family={Chocyk}, + familyi={C\bibinitperiod}, + given={D.}, + giveni={D\bibinitperiod}}}% + {{hash=fa359615394426dff04c6f196de50a92}{% + family={Skic}, + familyi={S\bibinitperiod}, + given={A.}, + giveni={A\bibinitperiod}}}% + {{hash=735ac71614372e54c2c5b12c4a8b2037}{% + family={Kamiński}, + familyi={K\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + {{hash=80f5de14d028c35ed21c52a0993eb44e}{% + family={Macek}, + familyi={M\bibinitperiod}, + given={W.}, + giveni={W\bibinitperiod}}}% + {{hash=2458b153bc1351893a163117b0b687eb}{% + family={Turek}, + familyi={T\bibinitperiod}, + given={M.}, + giveni={M\bibinitperiod}}}% + } + \list{language}{1}{% + {English}% + } + \strng{namehash}{0c580510ffd19c48fb276fd9bcbd3cc8} + \strng{fullhash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{fullhashraw}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{bibnamehash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authorbibnamehash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authornamehash}{0c580510ffd19c48fb276fd9bcbd3cc8} + \strng{authorfullhash}{ed8bfd0d39c94dcd76e642641bd4b638} + \strng{authorfullhashraw}{ed8bfd0d39c94dcd76e642641bd4b638} + \field{sortinit}{5} + \field{sortinithash}{20e9b4b0b173788c5dace24730f47d8c} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{From the wide range of engineering materials traditional Stellite 6 (cobalt alloy) exhibits excellent resistance to cavitation erosion (CE). Nonetheless, the influence of ion implantation of cobalt alloys on the CE behaviour has not been completely clarified by the literature. Thus, this work investigates the effect of nitrogen ion implantation (NII) of HIPed Stellite 6 on the improvement of resistance to CE. Finally, the cobalt-rich matrix phase transformations due to both NII and cavitation load were studied. The CE resistance of stellites ion-implanted by 120 keV N+ ions two fluences: 5*1016 cm-2 and 1*1017 cm-2 were comparatively analysed with the unimplanted stellite and AISI 304 stainless steel. CE tests were conducted according to ASTM G32 with stationary specimen method. Erosion rate curves and mean depth of erosion confirm that the nitrogen-implanted HIPed Stellite 6 two times exceeds the resistance to CE than unimplanted stellite, and has almost ten times higher CE reference than stainless steel. The X-ray diffraction (XRD) confirms that NII of HIPed Stellite 6 favours transformation of the "(hcp) to (fcc) structure. Unimplanted stellite "-rich matrix is less prone to plastic deformation than and consequently, increase of phase effectively holds carbides in cobalt matrix and prevents Cr7C3 debonding. This phenomenon elongates three times the CE incubation stage, slows erosion rate and mitigates the material loss. Metastable structure formed by ion implantation consumes the cavitation load for work-hardening and ! " martensitic transformation. In further CE stages, phases transform as for unimplanted alloy namely, the cavitation-inducted recovery process, removal of strain, dislocations resulting in increase of phase. The CE mechanism was investigated using a surface profilometer, atomic force microscopy, SEM-EDS and XRD. HIPed Stellite 6 wear behaviour relies on the plastic deformation of cobalt matrix, starting at Cr7C3/matrix interfaces. Once the Cr7C3 particles lose from the matrix restrain, they debond from matrix and are removed from the material. Carbides detachment creates cavitation pits which initiate cracks propagation through cobalt matrix, that leads to loss of matrix phase and as a result the CE proceeds with a detachment of massive chunk of materials. © 2021 by the authors.} + \field{issn}{19961944 (ISSN)} + \field{journaltitle}{Materials} + \field{note}{Publisher: MDPI AG} + \field{number}{9} + \field{title}{Effect of nitrogen ion implantation on the cavitation erosion resistance and cobalt-based solid solution phase transformations of {HIPed} stellite 6} + \field{volume}{14} + \field{year}{2021} + \verb{doi} + \verb 10.3390/ma14092324 + \endverb + \verb{urlraw} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-85105941706&doi=10.3390%2fma14092324&partnerID=40&md5=4c846be7d06977d42697c88c326e5923 + \endverb + \verb{url} + \verb https://www.scopus.com/inward/record.uri?eid=2-s2.0-85105941706&doi=10.3390%2fma14092324&partnerID=40&md5=4c846be7d06977d42697c88c326e5923 + \endverb + \keyw{AISI-304 stainless steel,Atomic force microscopy,Carbides,Cavitation,Cavitation erosion,Cavitation erosion resistance,Chromium compounds,Cobalt alloy,Cobalt alloys,Cracks propagation,Damage mechanism,Engineering materials,Erosion,Failure analysis,Ion implantation,Ions,Linear transformations,Martensitic transformations,Mean depth of erosions,Metastable structures,Nitrogen,Nitrogen ion implantations,Phase transformation,Plastic deformation,Stellite,Stellite 6,Strain hardening,Surface profilometers,Wear,X ray diffraction} + \endentry + \entry{thiruvengadamTheoryErosion1967}{article}{}{} + \name{author}{1}{}{% + {{hash=d3cae98a50611da092efbc498a5a497c}{% + family={Thiruvengadam}, + familyi={T\bibinitperiod}, + given={Alagu}, + giveni={A\bibinitperiod}}}% + } + \strng{namehash}{d3cae98a50611da092efbc498a5a497c} + \strng{fullhash}{d3cae98a50611da092efbc498a5a497c} + \strng{fullhashraw}{d3cae98a50611da092efbc498a5a497c} + \strng{bibnamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorbibnamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authornamehash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorfullhash}{d3cae98a50611da092efbc498a5a497c} + \strng{authorfullhashraw}{d3cae98a50611da092efbc498a5a497c} + \field{sortinit}{6} + \field{sortinithash}{b33bc299efb3c36abec520a4c896a66d} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{abstract}{An elementary theory of erosion is derived based on the assumptions of 'accumulation' and 'attenuation' of the energies of impact causing erosion. This theory quantitatively predicts the relative intensity of erosion as a function of relative time and this prediction is in fair agreement with experimental observations. Since the intensity of collision, the distance of shock transmission and the material failure are all statistical events, a generalization of the elementary theory is suggested. Some of the practical results of this theory are the predictions of the cumulative depth of erosion, the determination of erosion strength and the method of correlation with other parameters such as liquid properties and hydrodynamic factors. Modifications of this theory for brittle and viscoelastic materials are also suggested. (Author)} + \field{journaltitle}{Proc. 2nd Meersburg Conf. on Rain Erosion and Allied Phenomena} + \field{month}{3} + \field{title}{Theory of erosion} + \field{volume}{2} + \field{year}{1967} + \field{pages}{53} + \range{pages}{1} + \endentry + \enddatalist +\endrefsection + +\refsection{1} + \datalist[entry]{none/global//global/global/global} + \entry{C05}{misc}{}{} + \name{author}{1}{}{% + {{hash=fc13b91fcf8c46eeb4e62740272a1ba9}{% + family={Awesome}, + familyi={A\bibinitperiod}, + given={F.}, + giveni={F\bibinitperiod}}}% + } + \strng{namehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{bibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorbibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authornamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \field{extraname}{1} + \field{sortinit}{2} + \field{sortinithash}{8b555b3791beccb63322c22f3320aa9a} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{title}{Frank} + \field{year}{2005} + \true{nocite} + \keyw{mine} + \endentry + \entry{C06}{misc}{}{} + \name{author}{1}{}{% + {{hash=fc13b91fcf8c46eeb4e62740272a1ba9}{% + family={Awesome}, + familyi={A\bibinitperiod}, + given={F.}, + giveni={F\bibinitperiod}}}% + } + \strng{namehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{fullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{bibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorbibnamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authornamehash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhash}{fc13b91fcf8c46eeb4e62740272a1ba9} + \strng{authorfullhashraw}{fc13b91fcf8c46eeb4e62740272a1ba9} + \field{extraname}{2} + \field{sortinit}{3} + \field{sortinithash}{ad6fe7482ffbd7b9f99c9e8b5dccd3d7} + \field{labelnamesource}{author} + \field{labeltitlesource}{title} + \field{title}{frank, but lowercase} + \field{year}{2006} + \true{nocite} + \keyw{mine} + \endentry + \enddatalist +\endrefsection +\endinput + diff --git a/Thesis.lof b/Thesis.lof new file mode 100644 index 0000000..fee9bf6 --- /dev/null +++ b/Thesis.lof @@ -0,0 +1,10 @@ +\babel@toc {english}{}\relax +\contentsline {xpart}{Chapters}{2}{part.1}% +\addvspace {10\p@ } +\contentsline {xchapter}{Introduction}{2}{chapter.1}% +\addvspace {10\p@ } +\contentsline {xchapter}{Analytical Investigations}{8}{chapter.2}% +\addvspace {10\p@ } +\contentsline {xchapter}{Experimental Investigations}{9}{chapter.3}% +\addvspace {10\p@ } +\contentsline {xchapter}{Discussion}{10}{chapter.4}% diff --git a/Thesis.lot b/Thesis.lot new file mode 100644 index 0000000..9ee2365 --- /dev/null +++ b/Thesis.lot @@ -0,0 +1,11 @@ +\babel@toc {english}{}\relax +\contentsline {xpart}{Chapters}{2}{part.1}% +\addvspace {10\p@ } +\contentsline {xchapter}{Introduction}{2}{chapter.1}% +\contentsline {table}{\numberline {1.1}{\ignorespaces Stellite Compositions}}{4}{table.caption.7}% +\addvspace {10\p@ } +\contentsline {xchapter}{Analytical Investigations}{8}{chapter.2}% +\addvspace {10\p@ } +\contentsline {xchapter}{Experimental Investigations}{9}{chapter.3}% +\addvspace {10\p@ } +\contentsline {xchapter}{Discussion}{10}{chapter.4}% diff --git a/Thesis.maf b/Thesis.maf new file mode 100644 index 0000000..8f1b44e --- /dev/null +++ b/Thesis.maf @@ -0,0 +1,6 @@ +Thesis.mtc +Thesis.mtc0 +Thesis.mtc4 +Thesis.mtc3 +Thesis.mtc2 +Thesis.mtc1 diff --git a/Thesis.mtc b/Thesis.mtc new file mode 100644 index 0000000..e69de29 diff --git a/Thesis.mtc0 b/Thesis.mtc0 new file mode 100644 index 0000000..e69de29 diff --git a/Thesis.mtc1 b/Thesis.mtc1 new file mode 100644 index 0000000..3f1d6df --- /dev/null +++ b/Thesis.mtc1 @@ -0,0 +1,12 @@ +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.1}Table: Show the table of stellite compositions}{\reset@font\mtcSfont 3}{section.1.1}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.2}Table: Show the table of stellite compositions}{\reset@font\mtcSfont 3}{section.1.2}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.3}Paragraph 4: Synergistic Challenges in Applications Prone to Corrosion and Cavitation\hfill {}\textsc {ignore}}{\reset@font\mtcSfont 5}{section.1.3}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.4}Paragraph 5: Research and Development for Enhanced Corrosion and Cavitation Performance\hfill {}\textsc {ignore}}{\reset@font\mtcSfont 5}{section.1.4}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.5}Paragraph 6: Influence of HIPing\hfill {}\textsc {ignore}}{\reset@font\mtcSfont 5}{section.1.5}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.6}General Background}{\reset@font\mtcSfont 5}{section.1.6}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.7}Stellite 1}{\reset@font\mtcSfont 7}{section.1.7}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.8}Stellites}{\reset@font\mtcSfont 7}{section.1.8}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.9}Objectives and Scope of the Research Work}{\reset@font\mtcSfont 7}{section.1.9}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.10}Thesis Outline}{\reset@font\mtcSfont 7}{section.1.10}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.11}Literature Survey}{\reset@font\mtcSfont 7}{section.1.11}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {1.12}Cavitation Tests}{\reset@font\mtcSfont 7}{section.1.12}} diff --git a/Thesis.mtc2 b/Thesis.mtc2 new file mode 100644 index 0000000..e69de29 diff --git a/Thesis.mtc3 b/Thesis.mtc3 new file mode 100644 index 0000000..87e98a7 --- /dev/null +++ b/Thesis.mtc3 @@ -0,0 +1 @@ +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {3.1}Materials and Microstructure}{\reset@font\mtcSfont 9}{section.3.1}} diff --git a/Thesis.mtc4 b/Thesis.mtc4 new file mode 100644 index 0000000..b944881 --- /dev/null +++ b/Thesis.mtc4 @@ -0,0 +1,5 @@ +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {4.1}Experimental Test Procedure}{\reset@font\mtcSfont 10}{section.4.1}} +{\reset@font\mtcSSfont\mtc@string\contentsline{subsection}{\noexpand \leavevmode \numberline {4.1.1}Hardness Tests}{\reset@font\mtcSSfont 10}{subsection.4.1.1}} +{\reset@font\mtcSSfont\mtc@string\contentsline{subsection}{\noexpand \leavevmode \numberline {4.1.2}Cavitation}{\reset@font\mtcSSfont 10}{subsection.4.1.2}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {4.2}Relationships between cavitation erosion resistance and mechanical properties}{\reset@font\mtcSfont 10}{section.4.2}} +{\reset@font\mtcSfont\mtc@string\contentsline{section}{\noexpand \leavevmode \numberline {4.3}Influence of vibratory amplitude}{\reset@font\mtcSfont 10}{section.4.3}} diff --git a/Thesis.pdf b/Thesis.pdf new file mode 100644 index 0000000..6f72259 --- /dev/null +++ b/Thesis.pdf @@ -0,0 +1,3 @@ +version https://git-lfs.github.com/spec/v1 +oid sha256:e768a7480c7f5f4d9296dcb38053709c0338df7d9c82af92db9e48d304b0094d +size 219752 diff --git a/Thesis.tex b/Thesis.tex index 19eef82..e1e5909 100644 --- a/Thesis.tex +++ b/Thesis.tex @@ -1,119 +1,346 @@ -%%%% -%% This Source Code Form is subject to the terms of the MIT License. -%% If a copy of the MIT was not distributed with this file, You can obtain one at https://opensource.org/licenses/mit -%% -%% Last update: 2024/03/11 -%% -%% author: Dorian Gouzou -%% repository hosted on github at https://github.com/jackred/Heriot_Watt_Thesis_Template -%%%% -\documentclass[12pt,a4paper]{report} - +% Created 2025-05-11 ح 23:09 +% Intended LaTeX compiler: pdflatex +\documentclass[11pt]{report} +\usepackage[utf8]{inputenc} +\usepackage[T1]{fontenc} +\usepackage{graphicx} +\usepackage{longtable} +\usepackage{wrapfig} +\usepackage{rotating} +\usepackage[normalem]{ulem} +\usepackage{amsmath} +\usepackage{amssymb} +\usepackage{capt-of} +\usepackage{hyperref} +\usepackage{booktabs} +\graphicspath{{expt/}} \input{I-packages} \input{I-config} \input{I-info} \input{I-glossary} -\input{I-packages-2} % some package need to be loaded last in preamble +\input{I-packages-2} +% some package need to be loaded last in preamble +\usepackage{multirow} +\usepackage[flushleft]{threeparttable} % http://ctan.org/pkg/threeparttable +\usepackage{booktabs,caption} +\date{} +\title{} +\hypersetup{ + pdfauthor={Vishakh Pradeep Kumar}, + pdftitle={}, + pdfkeywords={}, + pdfsubject={}, + pdfcreator={Emacs 30.1 (Org mode 9.7.29)}, + pdflang={English}} +\usepackage{biblatex} \begin{document} \dominitoc \pagestyle{empty} -\input{Preliminaries/1-titlepages} +\input{preliminaries/1-titlepages} \clearpage % % remove this line if you don't want pagination on preliminary pages % % also read the comment below, for table of content and other % \pagestyle{preliminary} -\input{Preliminaries/2-abstract} +\input{preliminaries/2-abstract} \clearpage %\input{Preliminaries/3-dedication} %\clearpage -\input{Preliminaries/4-acknowledgments} +\input{preliminaries/4-acknowledgments} \clearpage % % read about declaration in file % % \input{Preliminaries/5-declaration} -\includepdf[pages=-]{Preliminaries/5-declaration.pdf} - +\includepdf[pages=-]{preliminaries/5-declaration.pdf} { - \setstretch{1} - \hypersetup{linkcolor=black} - \tableofcontents - \listoftables % optional - \listoffigures % optional - \glsaddall % this is to include all acronym. You can do a sort of citation for acronym and include only the one you use, Look at the glossary package for details. - \printnoidxglossary[type=\acronymtype, title=Glossary] % optional - %% put your publications in BibMine.bib - %% They will be displayed here - \begin{refsection}[BibMine.bib] - \DeclareFieldFormat{labelnumberwidth}{#1} - \nocite{*} - \printbibliography[omitnumbers=true,title={List of Publications}] - \end{refsection} +\setstretch{1} +\hypersetup{linkcolor=black} +\tableofcontents +\listoftables % optional +\listoffigures % optional +\glsaddall % this is to include all acronym. You can do a sort of citation for acronym and include only the one you use, Look at the glossary package for details. +\printnoidxglossary[type=\acronymtype, title=Glossary] % optional +%% put your publications in BibMine.bib +%% They will be displayed here +\begin{refsection}[BibMine.bib] +\DeclareFieldFormat{labelnumberwidth}{#1} +\nocite{*} +\printbibliography[omitnumbers=true,title={List of Publications}] +\end{refsection} } -%% if you don't want pagination you need to use this commented part instead of the one above for the table of content/list of figure/etc -%% this is because the toc is defined in an annoying way, especially multi page one -%% solution found here: https://tex.stackexchange.com/a/173423 -% { -% \hypersetup{linkcolor=black} -% \pagestyle{empty} % Removes numbers from middle pages. -% \fancypagestyle{plain} % Re-definition removes numbers from first page. -% { -% \fancyhf{}% % Clear all header and footer fields. -% \renewcommand{\headrulewidth}{0pt}% Clear rules (remove these two lines if not desired). -% \renewcommand{\footrulewidth}{0pt}% -% } -% \tableofcontents -% \thispagestyle{empty} -% \listoftables %optional -% \thispagestyle{empty} -% \listoffigures %optional -% \thispagestyle{empty} -% \glsaddall % this is to include all acronym. You can do a sort of citation for acronym and include only the one you use, Look at the glossary package for details. -% \printnoidxglossary[type=\acronymtype, title=Glossary] % optional -% \thispagestyle{empty} -% %% put your publications in BibMine.bib -% %% They will be displayed here -% \begin{refsection}[BibMine.bib] -% \DeclareFieldFormat{labelnumberwidth}{#1} -% \nocite{*} -% \printbibliography[omitnumbers=true,title={List of Publications}] -% \end{refsection} -% \thispagestyle{empty} -% } - - \clearpage - \pagestyle{chapter} -\subfile{Chapters/Cavitation} -\subfile{Chapters/Chapter1-Introduction} -\subfile{Chapters/Chapter2} -\subfile{Chapters/Chapter3} -\appendix -\subfile{Appendices/Appendix1} +\part{Chapters} +\label{sec:org3bdb98f} -%% add publications in pdf format -\clearpage -\stepcounter{chapter} -\addcontentsline{toc}{chapter}{\thechapter\ \ \ \ Publication 1} -\includepdf[pages=-]{Publications/Publication1.pdf} +\chapter{Introduction} +\label{sec:org28b34e8} -%% using biblatex rather than bibtex to easily have further reading and references -%% you need to remove the cache file when adding files to the bibliography -%% Log and output files > trash icons in Overleaf -%% sorted by citation -\label{Bibliography} -\printbibliography[title={References}, heading=bibintoc, resetnumbers=true] -%% sorted by alphabetical order, using author name -%\begin{refsection} -%\DeclareFieldFormat{labelnumberwidth}{#1} -%\nocite{*} -%\printbibliography[title={Bibliography}, notcategory=cited, omitnumbers=true, heading=bibintoc] -%\end{refsection} +Stellites are a cobalt-base superalloy used in aggresive service environments due to retention of strength, wear resistance, and oxidation resistance at high temperature \cite{ahmedStructurePropertyRelationships2014}. +Originating in 1907 with Elwood Haynes's development of alloys like Stellite 6, Stellites quickly found use in orthopedic implants, machine tools, and nuclear components, and new variations on the original CoCrWC and CoCrMoC alloys are spreading to new sectors like oil \& gas and chemical processing \cite{malayogluComparingPerformanceHIPed2003, ahmedStructurePropertyRelationships2014}. + +Stellites generally contain 25-33 wt Cr, 4-18 W/Mo, and 0.1-3.3 wt C, with a microstructure consisting of a CoCr(W,Mo) matrix with solid solution strengthening, with hard carbide phases, usually with Cr (e.g., \(M_{7}C_{3}\), \(M_{23}C_{6}\)), and W/Mo (e.g. \(MC\), \(M_{6}C\) ); the proportion and type of carbides depend on carbon content and the relative amounts of carbon with carbide formers (Cr, W, Mo), as well as processing routes. In addition to the solid solution toughness and carbide hardness, the stress-induced FCC tp HCP phase transformation of the Co-based solid solution further increases wear resistance through work hardening. + + + +The remarkable ability of Stellite alloys to withstand these specific challenges stems from key metallurgical features. Their corrosion resistance is primarily attributed to a high chromium content, typically 20-30 wt.\%, which promotes the formation of a highly stable, tenacious, and self-healing chromium-rich passive oxide film on the material's surface; this film acts as a barrier isolating the underlying alloy from the corrosive environment. Alloying elements such as molybdenum and tungsten can further enhance this passivity, particularly improving resistance to localized corrosion phenomena like pitting and crevice corrosion in aggressive media. Concurrently, their outstanding cavitation resistance is largely derived from the unique behavior of the cobalt-rich matrix, which can undergo a stress-induced crystallographic transformation from a face-centered cubic (fcc) to a hexagonal close-packed (hcp) structure. This transformation, often facilitated by mechanical twinning, effectively absorbs the intense, localized impact energy from collapsing cavitation bubbles and leads to significant work hardening, thereby impeding material detachment and erosion. + + +Stellites generally contain 25-33 wt Cr, 4-18 W/Mo, and 0.1-3.3 wt C, with a microstructure consisting of a CoCr(W,Mo) matrix with solid solution strengthening, with hard carbide phases, usually with Cr (e.g., \(M_{7}C_{3}\), \(M_{23}C_{6}\)), and W/Mo (e.g. \(MC\), \(M_{6}C\) ); the proportion and type of carbides depend on carbon content and the relative amounts of carbon with carbide formers (Cr, W, Mo), as well as processing routes. In addition to the solid solution toughness and carbide hardness, the stress-induced FCC tp HCP phase transformation of the Co-based solid solution further increases wear resistance through work hardening. +\section{Table: Show the table of stellite compositions} +\label{sec:org128a963} +\section{Table: Show the table of stellite compositions} +\label{sec:org513cc9c} + +\begin{LaTeX} +\begin{landscape} +\begin{table} +\caption{Stellite Compositions} +\label{tab:stellite_composition} +\begin{threeparttable} +\begin{tabular}{lllllllllllllllll} + & + \multicolumn{2}{c}{Base} & + \multicolumn{2}{c}{Refractory} & + Carbon & + \multicolumn{8}{c}{Others} & + & + & + \\ +Alloy & + \multicolumn{1}{c}{\textbf{Co}} & + \multicolumn{1}{c}{\textbf{Cr}} & + \multicolumn{1}{c}{\textbf{W}} & + \multicolumn{1}{c}{\textbf{Mo}} & + \multicolumn{1}{c}{\textbf{C}} & + \multicolumn{1}{c}{\textbf{Fe}} & + \multicolumn{1}{c}{\textbf{Ni}} & + \multicolumn{1}{c}{\textbf{Si}} & + \multicolumn{1}{c}{\textbf{P}} & + \multicolumn{1}{c}{\textbf{S}} & + \multicolumn{1}{c}{\textbf{B}} & + \multicolumn{1}{c}{\textbf{Ln}} & + \multicolumn{1}{c}{\textbf{Mn}} & + \multicolumn{1}{c}{\textbf{Ref}} & + \multicolumn{1}{c}{\textbf{Process Type}} & + \multicolumn{1}{c}{\textbf{Observation}} \\ + +\hline +\multirow{4}{*}{Stellite 1} +& 41.1 & 30.5 & 12.5 & & 2.4 & <5 & <3.5 & <2 & & & <1 & & <2 & \cite{davis2000nickel} & & \\ +& 47.7 & 30 & 13 & 0.5 & 2.5 & 3 & 1.5 & 1.3 & & & & & 0.5 & \cite{davis2000nickel} & & \\ +& 48.6 & 33 & 12.5 & 0 & 2.5 & 1 & 1 & 1.3 & & & & & 0.1 & \cite{alimardaniEffectLocalizedDynamic2010} & & \\ +& 46.84 & 31.7 & 12.7 & 0.29 & 2.47 & 2.3 & 2.38 & 1.06 & & & & & 0.26 & \cite{ahmedMappingMechanicalProperties2023} & HIPed & ICP-OES \\ + +\hline +\multirow{2}{*}{Stellite 3} +& 50.5 & 33 & 14 & & 2.5 & & & & & & & & & \cite{bunchCorrosionGallingResistant1989} & & \\ +& 49.24 & 29.57 & 12.07 & 0.67 & 2.52 & 2.32 & 1.07 & 1.79 & & & & & 0.75 & \cite{ratiaComparisonSlidingWear2019} & HIPed & ICP-OES and combustion infrared detection for C \\ + +\hline +\multirow{5}{*}{Stellite 4} +& 45.43 & 30 & 14 & 1 & 0.57 & 3 & 3 & 2 & & & & & 1 & \cite{davis2000nickel} & & \\ +& 51.5 & 30 & 14 & & 1 & 1 & 2 & 0.5 & & & & & & \cite{zhangFrictionWearCharacterization2002} & & \\ +& 51.9 & 33 & 14 & & 1.1 & & & & & & & & & \cite{bunchCorrosionGallingResistant1989} & & \\ +& 49.41 & 31 & 14 & 0.12 & 0.67 & 2.16 & 1.82 & 1.04 & & & & & 0.26 & \cite{ahmedMappingMechanicalProperties2023} & HIPed & ICP-OES \\ +& 50.2 & 29.8 & 14.4 & 0 & 0.7 & 1.9 & 1.9 & 0.8 & & & & & 0.3 & \cite{ashworthMicrostructurePropertyRelationships1999} & HIPed & \\ + +\hline +\multirow{10}{*}{Stellite 6} +& 51.5 & 28.5 & 4.5 & 1.5 & 1 & 5 & 3 & 2 & & & 1 & & 2 & \cite{davis2000nickel} & & \\ +& 63.81 & 27.08 & 5.01 & & 0.96 & 0.73 & 0.87 & 1.47 & & & & & 0.07 & \cite{ratiaComparisonSlidingWear2019} & HIPed & ICP-OES and combustion infrared detection for C \\ +& 60.3 & 29 & 4.5 & & 1.2 & 2 & 2 & 1 & & & & & & \cite{zhangFrictionWearCharacterization2002} & & \\ +& 61.7 & 27.5 & 4.5 & 0.5 & 1.15 & 1.5 & 1.5 & 1.15 & & & & & 0.5 & \cite{bunchCorrosionGallingResistant1989} & & \\ +& 58.46 & 29.5 & 4.6 & 0.22 & 1.09 & 2.09 & 2.45 & 1.32 & & & & & 0.27 & \cite{ahmedMappingMechanicalProperties2023} & HIPed & ICP-OES \\ +& 58.04 & 30.59 & 4.72 & & 1.24 & 2.03 & 1.87 & 0.80 & 0.01 & 0.01 & & & & \cite{ferozhkhanMetallurgicalStudyStellite2017} & PTAW & OES \\ +& 55.95 & 27.85 & 3.29 & & 0.87 & 6.24 & 3.63 & 1.23 & 0.01 & 0.01 & & & 0.45 & \cite{ferozhkhanMetallurgicalStudyStellite2017} & GTAW & OES \\ +& 52.40 & 30.37 & 3.57 & & 0.96 & 6.46 & 3.93 & 1.70 & 0.01 & 0.01 & & & 0.3 & \cite{ferozhkhanMetallurgicalStudyStellite2017} & SMAW & OES \\ +& 60.3 & & 31.10 & 4.70 & 0.30 & 1.10 & 1.70 & 1.50 & 1.30 & & 0.00 & & 0.3 & \cite{pacquentinTemperatureInfluenceRepair2025} & LP-DED & ICP-AES \& GDMS \\ +& 60.6 & 27.7 & 5 & 0 & 1.2 & 1.9 & 2 & 1.3 & & & & & 0.3 & \cite{ashworthMicrostructurePropertyRelationships1999} & HIPed & \\ + +\hline +Stellite 7 +& 64 & 25.9 & 4.9 & 0 & 0.5 & 1.5 & 1.1 & 1.1 & & & & & 1 & \cite{ashworthMicrostructurePropertyRelationships1999} & HIPed & \\ + +\hline +\multirow{2}{*}{Stellite 12} +& 53.6 & 30 & 8.3 & & 1.4 & 3 & 1.5 & 0.7 & & & & & 1.5 & \cite{davis2000nickel} & & \\ +& 55.22 & 29.65 & 8.15 & 0.2 & 1.49 & 2.07 & 2.04 & 0.91 & & & & & 0.27 & \cite{ahmedMappingMechanicalProperties2023} & HIPed & ICP-OES \\ + +Stellite 19 +& 50.94 & 31.42 & 10.08 & 0.79 & 2.36 & 1.82 & 2 & 0.4 & & & 0.09 & & 0.1 & \cite{desaiEffectCarbideSize1984} & & \\ + +\multirow{2}{*}{Stellite 20} +& 41.05 & 33 & 17.5 & & 2.45 & 2.5 & 2.5 & & & & & & 1 & \cite{davis2000nickel} & & \\ +& 43.19 & 31.85 & 16.3 & 0.27 & 2.35 & 2.5 & 2.28 & 1 & & & & & 0.26 & \cite{ahmedMappingMechanicalProperties2023} & HIPed & ICP-OES \\ + + +\multirow{2}{*}{Stellite 21} +& 59.493 & 27 & & 5.5 & 0.25 & 3 & 2.75 & 1 & & & 0.007 & & 1 & \cite{davis2000nickel} & & \\ +& 60.6 & 26.9 & 0 & 5.7 & 0.2 & 1.3 & 2.7 & 1.9 & & & & & 0.7 & \cite{ashworthMicrostructurePropertyRelationships1999} & HIPed & \\ + +Stellite 22 +& 54 & 27 & & 11 & 0.25 & 3 & 2.75 & 1 & & & & & 1 & \cite{davis2000nickel} & & \\ + +Stellite 23 +& 65.5 & 24 & 5 & & 0.4 & 1 & 2 & 0.6 & & & & & 0.3 & \cite{davis2000nickel} & & \\ + +Stellite 25 +& 49.4 & 20 & 15 & & 0.1 & 3 & 10 & 1 & & & & & 1.5 & \cite{davis2000nickel} & & \\ + +Stellite 27 +& 35 & 25 & & 5.5 & 0.4 & 1 & 32 & 0.6 & & & & & 0.3 & \cite{davis2000nickel} & & \\ + +Stellite 30 +& 50.5 & 26 & & 6 & 0.45 & 1 & 15 & 0.6 & & & & & 0.6 & \cite{davis2000nickel} & & \\ + +\multirow{2}{*}{Stellite 31} +& 57.5 & 22 & 7.5 & & 0.5 & 1.5 & 10 & 0.5 & & & & & 0.5 & \cite{davis2000nickel} & & \\ +& 52.9 & 25.3 & 7.8 & 0 & 0.5 & 1.1 & 11.4 & 0.6 & & & & & 0.4 & \cite{ashworthMicrostructurePropertyRelationships1999} & HIPed & \\ + +Stellite 80 +& 44.6 & 33.5 & 19 & & 1.9 & & & & & & 1 & & & \cite{davis2000nickel} & & \\ + +Stellite 188 +& 37.27 & 22 & 14 & & 0.1 & 3 & 22 & 0.35 & & & & 0.03 & 1.25 & \cite{davis2000nickel} & & \\ + +\multirow{2}{*}{Stellite 190} +& 46.7 & 27 & 14 & 1 & 3.3 & 3 & 3 & 1 & & & & & 1 & \cite{davis2000nickel} & & \\ +& 48.72 & 27.25 & 14.4 & 0.2 & 3.21 & 2.1 & 2.81 & 1 & & & & & 0.31 & \cite{ahmedMappingMechanicalProperties2023} & HIPed\tnote{a} & ICP-OES\tnote{*} \\ + +Stellite 300 +& 44.5 & 22 & 32 & & 1.5 & & & & & & & & & \cite{davis2000nickel} & & \\ + +Stellite 694 +& 45 & 28 & 19 & & 1 & 5 & & 1 & & & & & 1 & \cite{davis2000nickel} & & \\ + +Stellite 703 +& 44.6 & 32 & & 12 & 2.4 & 3 & 3 & 1.5 & & & & & 1.5 & \cite{davis2000nickel} & & \\ + +Stellite 706 +& 55.8 & 29 & & 5 & 1.2 & 3 & 3 & 1.5 & & & & & 1.5 & \cite{davis2000nickel} & & \\ + +Stellite 712 +& 51.5 & 29 & & 8.5 & 2 & 3 & 3 & 1.5 & & & & & 1.5 & \cite{davis2000nickel} & & \\ + +Stellite 720 +& 37.2 & 33 & & 18 & 2.5 & 3 & 3 & 1.5 & & & 0.3 & & 1.5 & \cite{davis2000nickel} & & \\ + +\end{tabular} +\begin{tablenotes} +\item[*] The footnote text. +\item[a] Another footnote. +\end{tablenotes} +\end{threeparttable} +\end{table} +\end{landscape} +\end{LaTeX} +\section{Paragraph 4: Synergistic Challenges in Applications Prone to Corrosion and Cavitation\hfill{}\textsc{ignore}} +\label{sec:org567a79b} + + +\section{Paragraph 5: Research and Development for Enhanced Corrosion and Cavitation Performance\hfill{}\textsc{ignore}} +\label{sec:org17e97e5} + + +\section{Paragraph 6: Influence of HIPing\hfill{}\textsc{ignore}} +\label{sec:org5332b96} + +Compared with the case alloys, the HIPed alloys had relatively finer, rounded, and distributed carbides. +\section{General Background} +\label{sec:org7bfce2d} +\%\% have a mini table of content at the start of the chapter +\{ +\hypersetup{linkcolor=black} +\minitoc +\} + +\%cite:@Franc2004265, @Romo201216, @Kumar2024, @Kim200685, @Gao2024, @20221xix, @Usta2023, @Cheng2023, @Zheng2022 + +Cavitation erosion presents a significant challenge in materials degradation in various industrial sectors, including hydroelectric power, marine propulsion, and nuclear systems, stemming from a complex interaction between fluid dynamics and material response \cite{francCavitationErosion2005, romoCavitationHighvelocitySlurry2012}. Hydrodynamically, the phenomenon initiates with the formation and subsequent violent collapse of vapor bubbles within a liquid, triggered by local pressures dropping to the saturated vapor pressure. These implosions generate intense, localized shockwaves and high-speed microjets that repeatedly impact adjacent solid surfaces \cite{gevariDirectIndirectThermal2020}. From a materials perspective, these impacts induce high stresses (100-1000 MPa) and high strain rates, surpassing material thresholds and leading to damage accumulation via plastic deformation, work hardening, fatigue crack initiation and propagation, and eventual material detachment. Mitigating this requires materials capable of effectively absorbing or resisting this dynamic loading, often under demanding conditions that may also include corrosion. + +Stellite alloys, cobalt-chromium formulations that contain carbon, tungsten and/or molybdenum, represent a critical class of materials renowned for their wear resistance in such harsh environments \cite{shinEffectMolybdenumMicrostructure2003}. Their performance stems from a composite-like microstructure combining a strong cobalt-rich matrix, strengthened by solid solutions of Cr and W/Mo, with hard carbide precipitates (e.g., M7C3, M23C6) that impede wear and crack propagation \cite{ahmedSlidingWearBlended2021a, crookCobaltbaseAlloysResist1994}. + +\% Martensitic transformation +Crucially, the cobalt matrix often possesses a low stacking fault energy, facilitating a strain-induced martensitic transformation from a metastable face-centered cubic \(\gamma\) phase to a hexagonal close-packed \(\epsilon\) phase under the intense loading of cavitation. This transformation is a primary mechanism for dissipating impact energy and enhancing work hardening, contributing significantly to Stellite's characteristic cavitation resistance \cite{huangMicrostructureEvolutionMartensite2023, tawancyFccHcpTransformation1986}. + +HIPing is a thermo-mechanical material processing technique which involves the simultaneous application of pressure (up to 200 MPa) and temperature (2000 C), which results in casting densification, porosity closure, and metallurgical bonding. \cite{yuComparisonTriboMechanicalProperties2007} + +While commonly applied via casting or weld overlays, processing routes like Hot Isostatic Pressing (HIP) offer potential advantages such as microstructure refinement \cite{stoicaInfluenceHeattreatmentSliding2005} finer microstructures and enhanced fatigue resistance \cite{ahmedInfluenceReHIPingStructure2013, yuComparisonTriboMechanicalProperties2007}. + +HIPing of surface coatings results in microstructure refinement, which can yield improved fatigue and fracture resistance. + +HIPing leads to carbide refinement, which can yield improved impact toughness \cite{yuInfluenceManufacturingProcess2008}, and reduce carbide brittleness \cite{yuComparisonTriboMechanicalProperties2007}. + +Furthermore, HIP facilitates the consolidation of novel 'blended' alloys created from mixed elemental or pre-alloyed powders, providing a pathway to potentially tailor compositions or microstructures for optimized performance. However, despite the prevalence of Stellite alloys and the known influence of processing on microstructure and properties, the specific cavitation erosion behavior of HIP-consolidated Stellites, particularly these blended formulations, remains underexplored in academic literature. Given that erosion mechanisms in Stellites often involve interactions at the carbide-matrix interface \cite{szalaEffectNitrogenIon2021}, understanding how HIP processing and compositional blending affect these interfaces and the matrix's transformative capacity under cavitation, especially when potentially coupled with corrosion, constitutes a critical knowledge gap addressed by this research. + + +\% Need to describe Stellite 1 +\section{Stellite 1} + +Stellite 1 is a high-carbon and high-tungsten alloy, making it suitable for demanding applications that require hardness \& toughness to combat sliding \& abrasive wear \cite{crookCobaltbaseAlloysResist1994} + + + + +\section{Stellites} +\section{Objectives and Scope of the Research Work} +\section{Thesis Outline} +\section{Literature Survey} +\section{Cavitation Tests} +\chapter{Analytical Investigations} +\label{sec:org23cd51a} +\chapter{Experimental Investigations} +\label{sec:orgcbd56dc} + +\section{Materials and Microstructure} +\label{sec:org409eb92} + +The HIPed alloy was produced via canning the gas-atomized powders at 1200C and 100 MPa pressure for 4h, while the cast alloys were produced via sand casting. +\% Sieve analysis and description of powders + +\% Refer to Table of chemical compositions of both cast and HIPed alloys. + +The microstructure of the alloys were observed via SEM in BSE mode, and the chemical compositions of the identified phases developed in the alloys were determined via EDS as well as with XRD under Cu \(K_{\alpha}\) radiation. + +Image analysis was also conducted to ascertain the volume fractions of individual phases. + + +The Vickers microhardness was measured using a Wilson hardness tester under loads of BLAH. Thirty measurements under each load were conducted on each sample. +\chapter{Discussion} +\label{sec:orgc69eb40} +\section{Experimental Test Procedure} + + + +\subsection{Hardness Tests} + + +\subsection{Cavitation} + + +\section{Relationships between cavitation erosion resistance and mechanical properties} + +\section{Influence of vibratory amplitude} + +\% Insert the whole spiel by that French dude about displacement and pressure (and then ruin it) +The pressure of the solution depends on the amplitude of the vibratory tip attached to the ultrasonic device. Under simple assumptions, kinetic energy of cavitation is proportional to the square of the amplitude and maximum hammer pressure is proportional to A. + +\begin{align} +x &= A sin(2 \pi f t) \\ +v &= \frac{dx}{dt} = 2 \pi f A sin(2 \pi f t) \\ +v_{max} &= 2 \pi f A \\ +v_{mean} &= \frac{1}{\pi} \int^\pi_0 A sin(2 \pi f t) = 4 f A \\ +\end{align} + +However, several researchers have found that erosion rates are not proportional to the second power of amplitude, but instead a smaller number. +Thiruvengadum \cite{thiruvengadamTheoryErosion1967} and Hobbs find that erosion rates are proportional to the 1.8 and 1.5 power of peak-to-peak amplitude. +Tomlinson et al find that erosion rate is linearly proportional to peak-to-peak amplitude in copper [3]. +Maximum erosion rate is approximately proportional to the 1.5 power of p-p amplitude [4]. +The propagation of ultrasonic waves may result in thermal energy absorption or into chemical energy, resulting in reduced power. For the purposes of converting data from studies that do not use an amplitude of 50um, a exponent factor of 1.5 has been applied. \end{document} - diff --git a/Preliminaries/1-titlepages.tex b/preliminaries/1-titlepages.tex similarity index 100% rename from Preliminaries/1-titlepages.tex rename to preliminaries/1-titlepages.tex diff --git a/Preliminaries/2-abstract.tex b/preliminaries/2-abstract.tex similarity index 100% rename from Preliminaries/2-abstract.tex rename to preliminaries/2-abstract.tex diff --git a/Preliminaries/3-dedication.tex b/preliminaries/3-dedication.tex similarity index 100% rename from Preliminaries/3-dedication.tex rename to preliminaries/3-dedication.tex diff --git a/Preliminaries/4-acknowledgments.tex b/preliminaries/4-acknowledgments.tex similarity index 100% rename from Preliminaries/4-acknowledgments.tex rename to preliminaries/4-acknowledgments.tex diff --git a/Preliminaries/5-declaration.pdf b/preliminaries/5-declaration.pdf similarity index 100% rename from Preliminaries/5-declaration.pdf rename to preliminaries/5-declaration.pdf diff --git a/Preliminaries/5-declaration.tex b/preliminaries/5-declaration.tex similarity index 100% rename from Preliminaries/5-declaration.tex rename to preliminaries/5-declaration.tex diff --git a/stellite.org b/stellite.org new file mode 100644 index 0000000..68f5a85 --- /dev/null +++ b/stellite.org @@ -0,0 +1,57 @@ + + +Overall Structure: A Progressive Unveiling of Stellite Alloys + +The introduction follows a logical progression: +- [ ] What they are and where they came from. + + [ ] Identification as Cobalt-base (Stellite) superalloys. + + [ ] Core beneficial properties + high strength, corrosion resistance, high-temperature hardness + + [ ] Pioneering figure (Elwood Haynes) and seminal alloy + Stellite 6 with nominal composition + + [ ] Brief mention of other significant early alloys and their initial scope of applications. +- [ ] Fundamental Strengthening Mechanisms + + [ ] Primary mechanism: Hard carbide precipitation (e.g., M$_{7}$C$_{3}$, M$_{23}$C$_{6}$), with dependence on carbon content and processing. + + [ ] Secondary mechanism: Solid solution strengthening by specific elements (W, Mo, Cr), also linked to carbon content. + + [ ] Additional mechanism: Stress-induced phase transformation (fcc to hcp) contributing to wear resistance via work hardening. +- [ ] How they are made and modified. +- [ ] Current research directions and future outlook. + + + + + +Cobalt-base (Stellite) superalloys are valued for their high strength, corrosion resistance, and hardness, especially at high temperatures. + +Originating in the early 1900s with Elwood Haynes's Stellite 6 (nominally Co–28Cr–4W–1.1C wt.%), these materials, alongside other early alloys like Vitallium and X-40, quickly found use in demanding applications, from industrial tools to aerospace components. + +Stellite alloys derive their properties from hard carbides (e.g., M$_{7}$C$_{3}$, M$_{23}$C$_{6}$), whose formation depends on carbon content and processing, and from solid solution strengthening by elements like W, Mo, and Cr, whose effect is also carbon-dependent. A stress-induced face-centered cubic (fcc) to hexagonal close-packed (hcp) phase transformation further enhances wear resistance through work hardening. + +Applications for Stellite alloys have expanded from traditional uses like machine tools and nuclear components to diverse sectors including oil and gas, chemical processing, and medical implants. This wider usage increases the demand for understanding their corrosion and tribo-corrosion performance in aggressive environments. + +Manufacturing processes critically influence Stellite's microstructure (which can be hypoeutectic or hypereutectic) and, consequently, its performance. Beyond traditional casting, modern powder metallurgy techniques like Hot Isostatic Pressing (HIPing) are favored for producing dense, homogenous, near-net shape parts, minimizing internal defects and subsequent machining. Surface engineering methods, including plasma transferred arc (PTA) welding and laser surface melting, further tailor surfaces for specific wear resistance needs, though considerations like substrate dilution effects on corrosion properties are important. + +Current research focuses on enhancing Stellite alloys through strategic alloying additions (e.g., Si, W, Mo) to tailor microstructure, mechanical properties, and corrosion behavior, partly by methods such as stabilizing the fcc phase. The integrity, protective qualities, and repassivation capability of their passive films are vital for resisting localized corrosion. Understanding the complex interplay between alloy composition, processing, microstructure, and performance in corrosive and wear-intensive conditions remains crucial for optimizing these alloys for existing and emerging industrial applications. + + + + + + + + +Cobalt-base (Stellite) alloys have seen extensive use in wear environments mainly due to their high strength, corrosion resistance and hardness Co-base superalloys rely primarily on carbides formed in the Co matrix and at grain boundaries for their strength and the distribution, size and shape of carbides depends on processing condition. Solid solution strengthening of Co-base alloy is normally provided by tantalum, tungsten, molybdenum, chromium and columbium [1]. Since these elements are all carbide formers their effectiveness in terms of solid solution strengthening is dependent on the C content of alloy. Stellite 6 with nominal composition Co–28Cr–4W–1.1C (wt.%) was the first Stellite alloy developed in 1900 by Elwood Haynes. In recent years, there have been investigations into the effect of additions of alloying elements [2] on the microstructure and mechanical properties of Stellite 6. Improved hardness through formation of intermetallic compounds and mixed carbides could be achieved in both cases. It was shown that W and Mo addition influences the corrosion behaviour by stabilising the fcc phase [1]. Recent work by Kuzucu et al. [3] has demonstrated how the addition of 6 wt.% Si can alter the microstructure and hardness of Stellite 6 alloy thus enabling the properties to be tailored towards a specific application. + + +Because Stellite alloys are often used to combat wear there have been numerous studies in which surface engineering strategies to functionalise the surface for a specific application have been assessed. These have included plasma transferred arc (PTA) welding [4], laser surface melting [5] and plasma diffusion treatments [6]. Currently use of Stellite alloys has extended into various industrial sectors (e.g. pulp and paper processing, oil and gas processing, pharmaceuticals, chemical processing) and the need for improving information regarding corrosion (and often tribo-corrosion) of Stellite alloys has increased. It has been recognised that processing changes, which affect the microstructure of Stellite alloy, will most probably affect the corrosion performance [7]. Mohamed et al. [7] in 1999 used dc electrochemical techniques to investigate the corrosion behaviour of crevice-containing and crevice-free Cast and Hot Isostatically Pressed (HIPed) Stellite 6 in 3% NaCl at ambient temperature. They concluded that Hot Isostatic Pressing (HIPing) could potentially improve the localised crevice and pitting corrosion resistance and related their findings to the crevice corrosion models developed by Oldfield and Sutton [8]. In a study by Kim and Kim [9], the corrosion resistance of PTA-welded surfaces was compared to spray-fused and open arc-welded surfaces. It was concluded that dilution effects, which change the composition due to mixing of the coating and the underlying substrate, are key issues in the corrosion resistance of welded layers and the PTA process in this respect was superior to the other two processes. + + +The compositional roots of contemporary cobalt-base superalloys stem from the early 1900s when patents covering the cobalt–chromium and cobalt–chromium–tungsten system were issued. Consequently, the Stellite alloys of E. Haynes became important industrial materials for cutlery, machine tools and wear-resistant hardfacing applications [1,2]. The cobalt–chromium–molybdenum casting alloy Vitallium was developed in the 1930s for dental prosthetics, and derivative HS-21 soon became an important material for turbocharger and gas turbine applications during the 1940s. Similarly, wrought cobalt–nickel–chromium alloy S816 was used extensively for both gas turbine blades and vanes during this period. Another key alloy, invented in about 1943 by R.H. ∗ Corresponding author. Present address: School of Mechanical Engineering, University of Leeds, Leeds LS2 9JT, UK. Tel.: +44 113 343 6812; fax: +44 113 242 4611. E-mail address: a.neville@leeds.ac.uk (A. Neville). 1 Present address: School of Mechanical Engineering, University of Leeds, Leeds LS2 9JT, UK. Thielemann, was cast cobalt–nickel–chromium–tungsten alloy X-40. This alloy is still used in gas turbine vanes and subsea drill bits, and it has served extensively as a model for newer generations of cobalt-base superalloys. Hot isostatic pressing (HIPing) is rapidly becoming an industry standard as a processing method. Due to increasingly complex engineering shape specifications, higher demands on quality and lowering costs, HIPing has matured to a stage where it is recognized universally and is used on an industrial scale. HIPing requires a high-pressure vessel and consists of applying high isostatic pressure, using an inert gas, to the surface of the piece being processed or on the surface of a can filled with powder. A resistance heater inside the pressure vessel provides the necessary heat for the treatment. The microstructures of Stellite alloys vary considerably with composition, manufacturing process and post treatment. They may either be in the form of hypoeutectic structure consisting of a Co-rich solid solution surrounded by eutectic carbides, or of the hypereutectic type containing large idiomorphic primary chromium-rich carbides and a eutectic [1] + +It is generally acknowledged that the susceptibility of passive metals to localised corrosion (including pitting) and the rate at which this corrosion process occurs are closely related to the ability of the passive film to resist breakdown and to repassivate once corrosion has initiated [2]. The chemical composition of the passive film, its structure, physical properties, coherence and thickness are of paramount importance in the nucleation and propagation of localised corrosion. Investigations into the composition and structure of passive oxide films on stainless steels and other related passive alloys are much more difficult than in the case of iron because the films are thinner, their chemical composition is complicated, and they cannot be reduced cathodically. A major part of the information available on composition and structure of passive films on stainless steels has been obtained with spectroscopic techniques, particularly X-ray photoelectron spectroscopy (XPS) and auger electron spectroscopy (AES). Other methods such as ion scattering spectroscopy (ISS) and secondary ion mass spectrometry (SIMS) also provide valuable data [3]. + +In the chemical, petrochemical and pump industries, machine parts often work in conditions where erosion and corrosion processes, acting together, are the main failure mechanisms. The deleterious synergistic effect of the erosion removes either corrosion product or the passive layer that is protecting the underlying surface. When a passive layer is removed, the time taken for it to repassivate is an important consideration in the assessment of wear rates. The rate of repassivation determines the amount of charge that can transfer when the surface is activated by an erosion event (e.g. impact of sand). The rate of repassivation in relation to the frequency of impact is an important consideration in erosion–corrosion. On stainless steels [1] it was shown that higher amounts of key elements (chromium, molybdenum) can lead a faster repassivation during erosion impacts. ∗ Corresponding author. Tel.: +44 113 343 6812; fax: +44 113 242 4611. E-mail address: a.neville@leeds.ac.uk (A. Neville). Cobalt-based alloys have enjoyed extensive use in wearrelated engineering applications for well over 50 years because of their inherent high-strength, corrosion resistance and ability to retain hardness at elevated temperatures [2]. In recent years a concentrated effort has been made to understand the deformation characteristics of cobalt-based alloys exposed to erosion–corrosion environments in order to optimize those factors contributing to their erosion resistance [3–5]. Alloying cobalt with chromium and various quantities of carbon, tungsten and molybdenum produces a family of alloys which can have excellent resistance to corrosion and/or erosion. Understanding how microstructural changes, as a result of alloying, affect corrosion and erosion resistance is critical to optimising the alloy for a particular purpose. In cobalt-based alloys, the key element chromium is added in the range of 20–30 wt.% to improve corrosion and impart some measure of solid-solution strengthening. Where carbide precipitation strengthening is a desirable feature, chromium also plays a strong role through the formation of a series of varying chromium–carbon ratio carbides such as M7C3 and M23C6. Alloying elements like tungsten, molybdenum and 0043-1648/$ – see front matter © 2005 Elsevier B.V. All rights reserved. doi:10.1016/j.wear.2005.02.038 tantalum are added to cobalt for solid solution strengthening. If these metals are added in excess of their solubility, formation of carbides like MC and M6C is likely to occur. Shin et al. [6] investigated the effect of molybdenum on the microstructure and wear resistance properties of Stellite 6 hardfacing alloy. They showed that with an increase in molybdenum content, the M23C6 and M6C type carbides were formed instead of chromium-rich M7C3. They concluded that this microstructural change was responsible for the improvement of the mechanical properties such as hardness and wear resistance of molybdenum-modified Stellite 6 hardfacing alloy. Most cobalt-based alloys possess outstanding cavitation resistance compared to stainless steels which has been shown to be independent of the carbon content (hence hardness), and has been attributed by Crook [7] to crystallographic transformation, under stress, from the face centred cubic (fcc) to hexagonal close packed (hcp) structure by twinning. Heathcock and Ball [8] studied the cavitation resistance of a number of Stellite alloys, cemented carbides and surface-treated alloy steels and showed that in Stellite alloys the cobalt-rich solid solution, incorporating elements such as chromium, tungsten and molybdenum is highly resistant to erosion due to a rapid increase in the work-hardening rate and the strain to fracture which are caused by deformation twinning. Lee et al. [9] compared the liquid impact erosion resistance of 12 Cr steel with a Vickers hardness of 380 kg/mm2 (∼39 MPa) and Stellite 6B with a hardness value of 420 kg/mm2 (∼43 MPa). The liquid impact erosion resistance of Stellite 6B was at least six times greater than that of 12 Cr steel, implying that hardness is not the governing factor for liquid erosion. Stellite 6B also showed very different behaviour in liquid impact erosion in comparison with 12 Cr steel. They concluded that the superior erosion resistance of Stellite 6B results from the cobalt matrix whose deformation appeared mostly as mechanical twins and the material removal was more dominant in the hard carbide precipitates than in the ductile cobalt matrix. Wong-Kian [10] showed that Stellite coatings were advantageous for use in erosion–corrosion environments and can even function at relatively high temperatures. They reported that this is because wear resistance is promoted by the harder complex carbides of chromium and tungsten, while corrosion resistance is enhanced by the presence of cobalt in the matrix. + +Cobalt-base alloys are now progressively used in many industrial and other applications. This is basically due to their high-temperature mechanical strength and their corrosion resistance in many environments. Some categories of these alloys may be used as high-temperature structural materials, wear resistant materials in aggressive media or for orthopedic implants. The main alloying elements are usually Cr, MO, W and Ni. Additionally, wear resistant alloys normally contain relatively high levels of carbon (0.25 to 2.5 wt.%) needed for carbide formation, while alloys used for structural applications are normally low in carbon. Alloy Stellite-6 is a Co—Cr—W—C alloy which exhibits an outstanding oxidation and corrosion resistance, hightemperature strength as well as resistance to thermal fatigue. The wrought alloy is used in nuclear and other industrial engineering purposes [1 to 4]. In nuclear industry, Stellite-6 is one of the most popular alloys used in manufacturing control and safety valve components in pressurized water reactors (PWR). It has also been used for control shaft guide bushings in sodium cooled reactors (LMFBR). In chemical industry, the alloy is used in the form of weld overlay for catalytic reactor valves for various liquids to resist the effect of corrosive wear and for surfacing of combustion engine valves and steam turbine valves. Powder metallurgy (PIM) is a fabrication technology capable of producing reasonably complex designs at relatively high rates of production. Using P/M technology, segregation problems (normally associated with conventional casting techniques) are minimized, especially for small parts. The metallurgical characteristics of the end product are primarily developed during the sintering cycle [5, 6]. Powder metallurgy techniques have been applied for the production of cobalt-base alloys. Two basic P/M techniques, namely hot isostatic pressing (HIP) and wet powder pouring (WPP) have been used for production of alloy Stellite-6. Details of these processes are described elsewhere [7, 8]. + +Cobalt-base (Stellite) alloys have seen extensive use in wear environments mainly due to their high strength, corrosion resistance and hardness. Co-base superalloys rely primarily on carbides, formed in the Co matrix and at grain boundaries, for their strength and wear resistance. The distribution, size and shape of carbides depend on processing conditions. Solid solution strengthening of Co-base alloys is normally provided by tantalum, tungsten, molybdenum, chromium and niobium [1]. Since these elements are all carbide formers, their effectiveness in terms of solid solution strengthening is dependent on the C content of the alloy. Stellite 6 with nominal composition Co–28Cr–4.5W–1.2C (wt%) was the first Stellite alloy developed in the early 1900s by Elwood Haynes. In recent years there have been investigations into the effect of alloying elements additions on the microstructure and mechanical properties of Stellite 6 [2]. Improved hardness through formation of intermetallic compounds and mixed carbides was achieved in both cases. It has been shown that adding W and Mo influences corrosion behaviour by stabilizing the face-centred cubic (fcc) phase [1]. ∗ Corresponding author. Tel.: +39 011 0904641; fax: +39 0110904699. E-mail address: francesco.rosalbino@polito.it (F. Rosalbino). Because Stellite alloys are often used to combat wear, there have been numerous studies into surface engineering strategies to functionalize the surface for a specific application. These have included plasma transferred arc (PTA) welding [3], laser surface melting [4] and plasma diffusion treatments [5] all involving Stellite alloys. Application of Co-base superalloys was traditionally most prevalent in the nuclear industry in the 1960s and 1970s and, for this reason, much research into corrosion of Stellite focused on conditions relating to nuclear power applications such as simulated PWR primary heat transfer conditions [6,7]. Currently, use of Stellite alloys has extended into various industrial sectors (e.g. pulp and paper processing, oil and gas processing, pharmaceuticals, chemical processing) and the need for improved information regarding corrosion (and often tribo-corrosion) of Stellite has increased. It has been recognized that processing changes, which affect the microstructure of Stellite alloys, most affect corrosion performance [8]. Hot isostatic pressing (HIPing) is a thermo-mechanical process [9] in which components or a contained powder is subjected to simultaneous applications of heat and high pressure in an inert medium. HIPing removes internal void cavities thus consolidating the structure making it homogenous, segregation free, dense, nearnet shape and requiring little or no machining. diff --git a/thesis.org b/thesis_original.org similarity index 100% rename from thesis.org rename to thesis_original.org