1. This document analyzes the mechanical properties and microstructure of Mo-Re alloys and welds with 0-50% Re content, both as-received and after electron beam welding and/or neutron irradiation.
2. It finds that increasing Re content improves properties like strength, plasticity, and creep resistance due to the "rhenium effect." Mo-Re welds exhibit large radiation-induced strengthening, especially at high temperatures.
3. Neutron irradiation is shown to cause intensified nucleation of Re-rich sigma phases in Mo-Re alloys, resulting in similar strength levels across irradiated welds.
Preparation and Investigation on Properties of Cryogenically Solidified Nano ...IJERA Editor
In the present work, AL-alloy containing 12% silicon (LM 13) matrix nano composites were fabricated in sand moulds by using copper end blocks of copper end chill thickness 10 &15 nm with cryogenic effect . The size of the reinforcement (NanoZro2) ranges from 50-80nm being added ranges from 3 to 15 wt % in steps of 3 wt % . Cryogenically solidified Nano Metal Matrix Composites were compressed by using hydraulic compression machine. Specimens were prepared according to ASTM standards and tested for their strength, hardness and fracture toughness. Micro structural studies of the fabricated Nano Composites indicate that there is uniform distributions of reinforcements in the matrix materials (LM 13). An increasing trend of hardness, UTS & fracture toughness has been observed. The best results have been obtained at 12 wt %. The results were further justified by comparing two copper end chill thickness 10 &15 mm. Finally the Volumetric Heat Capacity of the cryo-chill is identified as an important parameter which affects mechanical properties.
Effect of cyclic deformation damage on the corrosion of metastable austenitic...Chayon Mondal
This document summarizes an experiment on the effect of cyclic deformation damage on the corrosion rate of metastable austenitic stainless steels. The experiment subjected samples of 304 stainless steel to low cycle fatigue testing at different strain amplitudes to induce martensite formation. The amount of martensite and stored energy in the samples was then quantified. Finally, potentiodynamic polarization corrosion tests were performed on the samples in different solutions to analyze how martensite formation affected corrosion rates. The results showed that higher cyclic deformation and martensite content increased corrosion susceptibility. In conclusion, strain-induced martensite formation enhances corrosion susceptibility as confirmed by the polarization tests.
The document describes a study where MoSi2–Al2O3 nano-composite powder was prepared by mechanical alloying of MoO3, Si, and Al powders. Within short milling times (15-60 minutes depending on ball-to-powder weight ratio), a combustion process occurred that was characterized as a mechanically activated self-propagating high-temperature synthesis. This resulted in the complete reduction of MoO3 by Al and formation of MoSi2 and Al2O3 nano-composite powder. Further milling reduced crystallite sizes and increased lattice microstrain in the product phases. Addition of stearic acid as a process control agent postponed the reaction initiation and reduced crystallite sizes.
A novel aluminum based nanocomposite with high strength and good ductilityHossein Ramezanalizadeh
This document summarizes a research study that fabricated an aluminum-based nanocomposite containing nano-sized Al3Mg2 reinforcing particles. Aluminum and Al3Mg2 powders were mechanically milled and mixed at different times, then hot extruded to consolidate. Testing showed the nanocomposite exhibited high strength and good ductility compared to conventional aluminum, with strength increasing with longer milling time up to 15 hours due to grain refinement and homogeneous particle distribution. The interface between aluminum and Al3Mg2 particles also improved with milling time. Transmission electron microscopy revealed a clean interface with intimate contact between phases.
Micro Structure Amd Mechanical Properties of Nanoparticulate Wc/Al Metal Matr...IJRES Journal
The addition of reinforcement definitely changes mechanical behaviour of metal matrix composites (MMCs). Hence the objective of the work is to study the effect of nano WC particle content on the mechanical behaviour of Al alloy reinforced composites was studied by using optical microscopy, mechanical properties measurements and scanning electron microscope. The hardness, ultimate tensile strength, compression strength and young's modulus were found higher than those of control alloy. The dislocations which serve as heterogeneous nucleation sites for strengthening precipitates during subsequent solidification compared to control alloy. Higher density of dislocations and higher density of intermediate precipitates was observed.
Mechanochemical reduction of MoO3 powder by silicone to synthesize nanocrysta...Hossein Ramezanalizadeh
1) The document describes a study where mechanical alloying was used to synthesize nanocrystalline MoSi2 powder directly from molybdenum oxide (MoO3) and silicon (Si) powders.
2) X-ray diffraction analysis showed that within 6 hours of milling, MoO3 was fully converted to MoO2, and after 17 hours milling, peaks indicated the presence of both α and β phases of MoSi2 as well as Mo.
3) After 50 hours of milling, calculations showed the MoSi2 crystallite sizes were less than 100 nm, and the β-MoSi2 phase transformed to the α-MoSi2 phase.
Preparation and Investigation on Properties of Cryogenically Solidified Nano ...IJERA Editor
In the present work, AL-alloy containing 12% silicon (LM 13) matrix nano composites were fabricated in sand moulds by using copper end blocks of copper end chill thickness 10 &15 nm with cryogenic effect . The size of the reinforcement (NanoZro2) ranges from 50-80nm being added ranges from 3 to 15 wt % in steps of 3 wt % . Cryogenically solidified Nano Metal Matrix Composites were compressed by using hydraulic compression machine. Specimens were prepared according to ASTM standards and tested for their strength, hardness and fracture toughness. Micro structural studies of the fabricated Nano Composites indicate that there is uniform distributions of reinforcements in the matrix materials (LM 13). An increasing trend of hardness, UTS & fracture toughness has been observed. The best results have been obtained at 12 wt %. The results were further justified by comparing two copper end chill thickness 10 &15 mm. Finally the Volumetric Heat Capacity of the cryo-chill is identified as an important parameter which affects mechanical properties.
Effect of cyclic deformation damage on the corrosion of metastable austenitic...Chayon Mondal
This document summarizes an experiment on the effect of cyclic deformation damage on the corrosion rate of metastable austenitic stainless steels. The experiment subjected samples of 304 stainless steel to low cycle fatigue testing at different strain amplitudes to induce martensite formation. The amount of martensite and stored energy in the samples was then quantified. Finally, potentiodynamic polarization corrosion tests were performed on the samples in different solutions to analyze how martensite formation affected corrosion rates. The results showed that higher cyclic deformation and martensite content increased corrosion susceptibility. In conclusion, strain-induced martensite formation enhances corrosion susceptibility as confirmed by the polarization tests.
The document describes a study where MoSi2–Al2O3 nano-composite powder was prepared by mechanical alloying of MoO3, Si, and Al powders. Within short milling times (15-60 minutes depending on ball-to-powder weight ratio), a combustion process occurred that was characterized as a mechanically activated self-propagating high-temperature synthesis. This resulted in the complete reduction of MoO3 by Al and formation of MoSi2 and Al2O3 nano-composite powder. Further milling reduced crystallite sizes and increased lattice microstrain in the product phases. Addition of stearic acid as a process control agent postponed the reaction initiation and reduced crystallite sizes.
A novel aluminum based nanocomposite with high strength and good ductilityHossein Ramezanalizadeh
This document summarizes a research study that fabricated an aluminum-based nanocomposite containing nano-sized Al3Mg2 reinforcing particles. Aluminum and Al3Mg2 powders were mechanically milled and mixed at different times, then hot extruded to consolidate. Testing showed the nanocomposite exhibited high strength and good ductility compared to conventional aluminum, with strength increasing with longer milling time up to 15 hours due to grain refinement and homogeneous particle distribution. The interface between aluminum and Al3Mg2 particles also improved with milling time. Transmission electron microscopy revealed a clean interface with intimate contact between phases.
Micro Structure Amd Mechanical Properties of Nanoparticulate Wc/Al Metal Matr...IJRES Journal
The addition of reinforcement definitely changes mechanical behaviour of metal matrix composites (MMCs). Hence the objective of the work is to study the effect of nano WC particle content on the mechanical behaviour of Al alloy reinforced composites was studied by using optical microscopy, mechanical properties measurements and scanning electron microscope. The hardness, ultimate tensile strength, compression strength and young's modulus were found higher than those of control alloy. The dislocations which serve as heterogeneous nucleation sites for strengthening precipitates during subsequent solidification compared to control alloy. Higher density of dislocations and higher density of intermediate precipitates was observed.
Mechanochemical reduction of MoO3 powder by silicone to synthesize nanocrysta...Hossein Ramezanalizadeh
1) The document describes a study where mechanical alloying was used to synthesize nanocrystalline MoSi2 powder directly from molybdenum oxide (MoO3) and silicon (Si) powders.
2) X-ray diffraction analysis showed that within 6 hours of milling, MoO3 was fully converted to MoO2, and after 17 hours milling, peaks indicated the presence of both α and β phases of MoSi2 as well as Mo.
3) After 50 hours of milling, calculations showed the MoSi2 crystallite sizes were less than 100 nm, and the β-MoSi2 phase transformed to the α-MoSi2 phase.
The microstructural revolution of al 10%al3 mg2 nanocomposite during mechanic...Hossein Ramezanalizadeh
The document describes a study on the microstructural evolution of an Al-10% Al3Mg2 nanocomposite during mechanical milling. Pure Al and Mg were used to produce an Al3Mg2 intermetallic compound, which was then milled to produce fine Al3Mg2 powder. An Al-10% Al3Mg2 nanocomposite was fabricated after different milling times. XRD analysis showed that the Al3Mg2 crystallite size decreased with increased milling time, while lattice strain increased. SEM revealed uniform distribution of nano-sized Al3Mg2 particles in the Al matrix after longer milling. The mechanism was identified as ductile-brittle, where brittle Al3Mg2
Fabrication and hardness investigation of Al-15%Mg2Si-3%Cu in-situ cast compo...Hossein Ramezanalizadeh
This document summarizes a study that fabricated an Al-15%Mg2Si metal matrix composite containing 3% copper via an in situ casting route. Microstructural characterization found that the addition of copper resulted in the formation of copper-rich intermetallic phases during solidification, reducing the size of primary Mg2Si particles from approximately 20 micrometers to 7 micrometers. Hardness testing showed that these intermetallic phases led to an increase in hardness of the composite compared to one without copper. The composite's lightweight Mg2Si phases make it suitable for applications requiring high specific stiffness and strength, such as in the aerospace and automotive industries.
Characteristics of Hypoeutectic Cu-Zr Alloy Rods Manufactured by Vertical Upw...Rautomead Limited
The focus in this study is therefore on applying a vertical upwards continuous casting (VUCC) mass-production
method to the pilot-scale manufacturing of Cu-Zr alloy rods. The microstructure and physical characteristics of these
VUCC rods were subsequently investigated and compared with rods produced by CMC. In addition, the wire-drawing
capability of the VUCC rods was examined, and the adaptability of the VUCC method to the mass production of
hypoeutectic Cu-Zr alloys was fully investigated.
2.
Investigation of the distribution of lead in three different combinations of ...Rautomead Limited
The main objective of this paper was to assess three leaded
brass samples (pending application with Copper Development
Association) using optical microscopy and mass
spectrometry to compare the distribution of lead. Based on
the mass spectrometry data, a great deal of variation was
not found within each of the samples based on five different
sample locations. Optical microscopy, scanning electron
microscopy and energy-dispersive X-ray spectroscopy
confirmed that the lead was homogenously distributed in
brass.
Study on hardening mechanisms in aluminium alloysIJERA Editor
The Al-Zn-Mg alloys are most commonly used age-hardenable aluminium alloys. The hardening mechanism is
further enhanced in addition of Sc. Sc additions to aluminium alloys are more promising. Due to the
heterogeneous distribution of nano-sized Al3Sc precipitates hardening effect can be accelerated. Mainly,
highlight on hardening mechanism in Al-Zn-Mg alloys with Sc effect is to study. In addition, several
characterisations have been done to age-hardening measurements at elevated temperatures from 120oC to 180
oC. The ageing kinetics has also been calculated from Arrhenius equation. Furthermore, friction stir processing
(FSP) can be introduced to surface modification process and hardened the cast aluminium alloys. In this study,
hardening mechanism can be evaluated by Vicker’s hardness measurement and mechanical testing is present
task.
Agglomeration of Ferro Manganese Fines for Use in LD Steel Making : Presented...PRABHASH GOKARN
This document summarizes research on agglomerating ferromanganese alloy fines to make them suitable for use in steelmaking. The researchers characterized the fines and tested various binders and agglomeration processes. Phenol-formaldehyde resin was found to produce agglomerates with sufficient strength. Laboratory and plant trials showed the agglomerates achieved manganese recovery comparable to lumps without introducing impurities to the steel. Commercialization of the agglomeration process provides an economical way to utilize alloy fines that were previously sold at a lower price.
This document discusses characterization of metal matrix composite properties by adding bronze and fly ash. It describes producing bronze-fly ash composites with 5%, 10%, 15%, and 20% fly ash content using stir casting. Testing found that hardness and tensile strength increased with higher fly ash content, while density decreased. Microstructural analysis using SEM showed fly ash was distributed throughout the matrix. In conclusion, fly ash up to 20% can be added to bronze composites through stir casting, increasing properties like hardness and tensile strength.
IOSR Journal of Mechanical and Civil Engineering (IOSR-JMCE) is an open access international journal that provides rapid publication (within a month) of articles in all areas of mechanical and civil engineering and its applications. The journal welcomes publications of high quality papers on theoretical developments and practical applications in mechanical and civil engineering. Original research papers, state-of-the-art reviews, and high quality technical notes are invited for publications.
Iaetsd fabrication and characterization of b4 cp particle reinforced lm24 al ...Iaetsd Iaetsd
This document describes research on fabricating and characterizing aluminum matrix composites reinforced with boron carbide (B4C) particles. LM24 aluminum alloy composites containing 1%, 2%, and 3% B4C by weight were produced using a compo casting method. Microstructural analysis found uniform distribution of B4C particles in the composites. Hardness and tensile tests showed the composites have superior mechanical properties compared to the unreinforced alloy, with hardness and tensile strength increasing with higher B4C content up to 3%. The composites were characterized using scanning electron microscopy and X-ray diffraction to analyze particle distribution and composition.
Briquetting of Ferro Manganese Fines & Use in Steel MakingPRABHASH GOKARN
Ferro Manganese(FeMn) is used for alloying & refining of steel. During manufacture of FeMn fines are generated which are not useable (except in small induction furnaces). This paper describes a process for agglomeration of FeMn fines and its use in steel making.
Paper submitted for NMD 2012.
Agglomeration of Ferroalloy Fines for use in Bulk Steelmaking ProcessesPRABHASH GOKARN
International Paper Published in STEEL TECH (ISSN 0976-4232) Vol:7 No:3 in April 2013
Ferroalloys are added as deoxidizing agents and additives to increase strength, elasticity and abrasion & corrosion resistance of steel. The preferred size of ferroalloy lumps for steel making is 10mm – 80 mm to optimize the operational efficiency. Ferroalloy lumps are produced by manual breaking of casted alloy cakes which generates 5-10% fines which cannot be used in bulk steel making process (like the commonly used LD process) because of handing and operational difficulties. Therefore, we at Tata Steel developed an agglomeration process for ferroalloy fines and used the briquettes thus produced for making steel. The developed process described in the paper is an economic, environment friendly and efficient way to utilize the ferroalloy fines in steel making.
Tribological study of Ceramic Matrix Composite(CMCs).pptxShibaSankarDash
Ceramic matrix composites (CMCs) have improved fracture toughness over conventional structural ceramics through the addition of fibers that increase crack resistance. This document discusses the tribological properties and wear mechanisms of various CMCs, including those reinforced with silicon carbide (SiC) fibers in a silicon nitride (Si3N4) matrix or carbon fibers in a silicon carbide (SiC) matrix. The lowest wear rates were found for zirconium diboride (ZrB2) composites containing 8-32% aluminum oxide (Al2O3). Proper material selection and microstructure optimization can improve CMC reliability and performance in tribological applications.
Comparison of rebound numbers for m20 concrete with silica fumeeSAT Publishing House
IJRET : International Journal of Research in Engineering and Technology is an international peer reviewed, online journal published by eSAT Publishing House for the enhancement of research in various disciplines of Engineering and Technology. The aim and scope of the journal is to provide an academic medium and an important reference for the advancement and dissemination of research results that support high-level learning, teaching and research in the fields of Engineering and Technology. We bring together Scientists, Academician, Field Engineers, Scholars and Students of related fields of Engineering and Technology.
Effect of different types of steel fibers with metakaolin & flyIAEME Publication
The document discusses an experimental study on the effect of different types of steel fibers with metakaolin and fly ash on the mechanical properties of high strength concrete. Three types of steel fibers were used at volumes ranging from 0.5% to 4% by weight of cementitious material. The addition of metakaolin and fly ash at 5% and 10% by weight improved the concrete properties. The results showed that compressive strength increased with steel fiber content up to 3.5%, with round crimped steel fibers performing best. Similarly, split tensile strength also increased up to 3.5% fiber content, with flat crimped fibers giving the highest strength. The study concluded that steel fibers improve the ductility of high
SiC and ZrO2 Weigh Percentage Effects on Microstructure of Al Based Matrix Co...INFOGAIN PUBLICATION
SiC and ZrO2 particle are succesfully reaction synthesized from powder of Al, ZrO2 and SiC using spark plasma sintering method. The XRD of sintered composite and microstructure of the aas-sintered products. With the ZrO2 content increasing, the grains are remarkably refined and the and the ZrO2 and nano SiC particles are dispersing more uniformly in Al matrix, forming a homogeneous structure with the least porosity.
Effect of secondary phase precipitation on the corrosion behavior of duplex ...Pedro Roman
This document summarizes the effect of secondary phase precipitation on the corrosion behavior of duplex stainless steels (DSSs). DSSs are susceptible to the formation of undesirable precipitates such as sigma, chi, and chromium-rich phases during heat treatment, welding, and prolonged high-temperature service. These secondary phases form due to diffusion processes between 700-950°C and spinodal decomposition between 350-550°C. The sigma phase precipitates preferentially at ferrite-austenite and ferrite-ferrite grain boundaries, depleting chromium and molybdenum and reducing corrosion resistance. Various characterization techniques can be used to detect these secondary phases and understand their impact on the corrosion properties of DSSs
DEVELOPMENT AND TRIBOLOGICAL CHARACTERIZATION OF DUAL PARTICLE AND TRIPLE PAR...ijmech
This document summarizes a study on the development and characterization of dual particle and triple particle aluminum metal matrix composites (Al-MMCs) reinforced with Al2O3 particles. Al-7075 alloy was reinforced with 10% volume fraction of Al2O3 particles with sizes ranging from 10-210 micrometers in dual and triple particle configurations. The composites were fabricated using stir casting and evaluated for microstructure, hardness, wear behavior, and density. Hardness and strength increased compared to unreinforced alloy, with triple particle composite exhibiting the highest values. Wear resistance was highest for dual particle composite. Density measurements found good casting quality with no porosity.
EFFECT OF ANTIMONY ADDITION RELATIVE TO MICROSTRUCTURE AND MECHANICAL PROPERT...Rautomead Limited
It is well documented that the addition of antimony in pure lead increases tensile strength and reduced elongation. The goal of the present work is to identify the cause of these phenomena by investigation of the effects of the addition of Sb (1.25%) on the structure of pure continuously cast lead and lead alloy rods. The microstructure and morphology of both pure lead and lead 1.25% antimony were examined by digital optical microscope and scanning electron microscope respectively. Energy Dispersive X-ray Spectroscopy (EDX) was used to identify alloying elements. The results showed that the effect of additions of antimony on mechanical properties of lead-antimony alloys is mainly due to the solid solubility of the antimony element. Homogenized distribution of the antimony results in a decrease in the grain size of the pure lead. These smaller grains mean higher strength so long as there is a homogeneous grain structure
This document lists the names of five Dutch businesses: a bakery located at a gas station in Purmerend, a gas station in Purmerend, a gas depot in Amsterdam, a gas station in Koog aan de Zaan, and the transportation company Vos Transport.
This document outlines a course map for mathematics courses, including prerequisites, developmental courses, college-level introductory courses, precalculus sequences, advanced courses, special placements, honors courses, and online homework systems. It provides information on placement into courses based on Combined CPT and SAT math scores and Regents exam scores. It also lists faculty web pages and resources available in the virtual learning commons.
The microstructural revolution of al 10%al3 mg2 nanocomposite during mechanic...Hossein Ramezanalizadeh
The document describes a study on the microstructural evolution of an Al-10% Al3Mg2 nanocomposite during mechanical milling. Pure Al and Mg were used to produce an Al3Mg2 intermetallic compound, which was then milled to produce fine Al3Mg2 powder. An Al-10% Al3Mg2 nanocomposite was fabricated after different milling times. XRD analysis showed that the Al3Mg2 crystallite size decreased with increased milling time, while lattice strain increased. SEM revealed uniform distribution of nano-sized Al3Mg2 particles in the Al matrix after longer milling. The mechanism was identified as ductile-brittle, where brittle Al3Mg2
Fabrication and hardness investigation of Al-15%Mg2Si-3%Cu in-situ cast compo...Hossein Ramezanalizadeh
This document summarizes a study that fabricated an Al-15%Mg2Si metal matrix composite containing 3% copper via an in situ casting route. Microstructural characterization found that the addition of copper resulted in the formation of copper-rich intermetallic phases during solidification, reducing the size of primary Mg2Si particles from approximately 20 micrometers to 7 micrometers. Hardness testing showed that these intermetallic phases led to an increase in hardness of the composite compared to one without copper. The composite's lightweight Mg2Si phases make it suitable for applications requiring high specific stiffness and strength, such as in the aerospace and automotive industries.
Characteristics of Hypoeutectic Cu-Zr Alloy Rods Manufactured by Vertical Upw...Rautomead Limited
The focus in this study is therefore on applying a vertical upwards continuous casting (VUCC) mass-production
method to the pilot-scale manufacturing of Cu-Zr alloy rods. The microstructure and physical characteristics of these
VUCC rods were subsequently investigated and compared with rods produced by CMC. In addition, the wire-drawing
capability of the VUCC rods was examined, and the adaptability of the VUCC method to the mass production of
hypoeutectic Cu-Zr alloys was fully investigated.
2.
Investigation of the distribution of lead in three different combinations of ...Rautomead Limited
The main objective of this paper was to assess three leaded
brass samples (pending application with Copper Development
Association) using optical microscopy and mass
spectrometry to compare the distribution of lead. Based on
the mass spectrometry data, a great deal of variation was
not found within each of the samples based on five different
sample locations. Optical microscopy, scanning electron
microscopy and energy-dispersive X-ray spectroscopy
confirmed that the lead was homogenously distributed in
brass.
Study on hardening mechanisms in aluminium alloysIJERA Editor
The Al-Zn-Mg alloys are most commonly used age-hardenable aluminium alloys. The hardening mechanism is
further enhanced in addition of Sc. Sc additions to aluminium alloys are more promising. Due to the
heterogeneous distribution of nano-sized Al3Sc precipitates hardening effect can be accelerated. Mainly,
highlight on hardening mechanism in Al-Zn-Mg alloys with Sc effect is to study. In addition, several
characterisations have been done to age-hardening measurements at elevated temperatures from 120oC to 180
oC. The ageing kinetics has also been calculated from Arrhenius equation. Furthermore, friction stir processing
(FSP) can be introduced to surface modification process and hardened the cast aluminium alloys. In this study,
hardening mechanism can be evaluated by Vicker’s hardness measurement and mechanical testing is present
task.
Agglomeration of Ferro Manganese Fines for Use in LD Steel Making : Presented...PRABHASH GOKARN
This document summarizes research on agglomerating ferromanganese alloy fines to make them suitable for use in steelmaking. The researchers characterized the fines and tested various binders and agglomeration processes. Phenol-formaldehyde resin was found to produce agglomerates with sufficient strength. Laboratory and plant trials showed the agglomerates achieved manganese recovery comparable to lumps without introducing impurities to the steel. Commercialization of the agglomeration process provides an economical way to utilize alloy fines that were previously sold at a lower price.
This document discusses characterization of metal matrix composite properties by adding bronze and fly ash. It describes producing bronze-fly ash composites with 5%, 10%, 15%, and 20% fly ash content using stir casting. Testing found that hardness and tensile strength increased with higher fly ash content, while density decreased. Microstructural analysis using SEM showed fly ash was distributed throughout the matrix. In conclusion, fly ash up to 20% can be added to bronze composites through stir casting, increasing properties like hardness and tensile strength.
IOSR Journal of Mechanical and Civil Engineering (IOSR-JMCE) is an open access international journal that provides rapid publication (within a month) of articles in all areas of mechanical and civil engineering and its applications. The journal welcomes publications of high quality papers on theoretical developments and practical applications in mechanical and civil engineering. Original research papers, state-of-the-art reviews, and high quality technical notes are invited for publications.
Iaetsd fabrication and characterization of b4 cp particle reinforced lm24 al ...Iaetsd Iaetsd
This document describes research on fabricating and characterizing aluminum matrix composites reinforced with boron carbide (B4C) particles. LM24 aluminum alloy composites containing 1%, 2%, and 3% B4C by weight were produced using a compo casting method. Microstructural analysis found uniform distribution of B4C particles in the composites. Hardness and tensile tests showed the composites have superior mechanical properties compared to the unreinforced alloy, with hardness and tensile strength increasing with higher B4C content up to 3%. The composites were characterized using scanning electron microscopy and X-ray diffraction to analyze particle distribution and composition.
Briquetting of Ferro Manganese Fines & Use in Steel MakingPRABHASH GOKARN
Ferro Manganese(FeMn) is used for alloying & refining of steel. During manufacture of FeMn fines are generated which are not useable (except in small induction furnaces). This paper describes a process for agglomeration of FeMn fines and its use in steel making.
Paper submitted for NMD 2012.
Agglomeration of Ferroalloy Fines for use in Bulk Steelmaking ProcessesPRABHASH GOKARN
International Paper Published in STEEL TECH (ISSN 0976-4232) Vol:7 No:3 in April 2013
Ferroalloys are added as deoxidizing agents and additives to increase strength, elasticity and abrasion & corrosion resistance of steel. The preferred size of ferroalloy lumps for steel making is 10mm – 80 mm to optimize the operational efficiency. Ferroalloy lumps are produced by manual breaking of casted alloy cakes which generates 5-10% fines which cannot be used in bulk steel making process (like the commonly used LD process) because of handing and operational difficulties. Therefore, we at Tata Steel developed an agglomeration process for ferroalloy fines and used the briquettes thus produced for making steel. The developed process described in the paper is an economic, environment friendly and efficient way to utilize the ferroalloy fines in steel making.
Tribological study of Ceramic Matrix Composite(CMCs).pptxShibaSankarDash
Ceramic matrix composites (CMCs) have improved fracture toughness over conventional structural ceramics through the addition of fibers that increase crack resistance. This document discusses the tribological properties and wear mechanisms of various CMCs, including those reinforced with silicon carbide (SiC) fibers in a silicon nitride (Si3N4) matrix or carbon fibers in a silicon carbide (SiC) matrix. The lowest wear rates were found for zirconium diboride (ZrB2) composites containing 8-32% aluminum oxide (Al2O3). Proper material selection and microstructure optimization can improve CMC reliability and performance in tribological applications.
Comparison of rebound numbers for m20 concrete with silica fumeeSAT Publishing House
IJRET : International Journal of Research in Engineering and Technology is an international peer reviewed, online journal published by eSAT Publishing House for the enhancement of research in various disciplines of Engineering and Technology. The aim and scope of the journal is to provide an academic medium and an important reference for the advancement and dissemination of research results that support high-level learning, teaching and research in the fields of Engineering and Technology. We bring together Scientists, Academician, Field Engineers, Scholars and Students of related fields of Engineering and Technology.
Effect of different types of steel fibers with metakaolin & flyIAEME Publication
The document discusses an experimental study on the effect of different types of steel fibers with metakaolin and fly ash on the mechanical properties of high strength concrete. Three types of steel fibers were used at volumes ranging from 0.5% to 4% by weight of cementitious material. The addition of metakaolin and fly ash at 5% and 10% by weight improved the concrete properties. The results showed that compressive strength increased with steel fiber content up to 3.5%, with round crimped steel fibers performing best. Similarly, split tensile strength also increased up to 3.5% fiber content, with flat crimped fibers giving the highest strength. The study concluded that steel fibers improve the ductility of high
SiC and ZrO2 Weigh Percentage Effects on Microstructure of Al Based Matrix Co...INFOGAIN PUBLICATION
SiC and ZrO2 particle are succesfully reaction synthesized from powder of Al, ZrO2 and SiC using spark plasma sintering method. The XRD of sintered composite and microstructure of the aas-sintered products. With the ZrO2 content increasing, the grains are remarkably refined and the and the ZrO2 and nano SiC particles are dispersing more uniformly in Al matrix, forming a homogeneous structure with the least porosity.
Effect of secondary phase precipitation on the corrosion behavior of duplex ...Pedro Roman
This document summarizes the effect of secondary phase precipitation on the corrosion behavior of duplex stainless steels (DSSs). DSSs are susceptible to the formation of undesirable precipitates such as sigma, chi, and chromium-rich phases during heat treatment, welding, and prolonged high-temperature service. These secondary phases form due to diffusion processes between 700-950°C and spinodal decomposition between 350-550°C. The sigma phase precipitates preferentially at ferrite-austenite and ferrite-ferrite grain boundaries, depleting chromium and molybdenum and reducing corrosion resistance. Various characterization techniques can be used to detect these secondary phases and understand their impact on the corrosion properties of DSSs
DEVELOPMENT AND TRIBOLOGICAL CHARACTERIZATION OF DUAL PARTICLE AND TRIPLE PAR...ijmech
This document summarizes a study on the development and characterization of dual particle and triple particle aluminum metal matrix composites (Al-MMCs) reinforced with Al2O3 particles. Al-7075 alloy was reinforced with 10% volume fraction of Al2O3 particles with sizes ranging from 10-210 micrometers in dual and triple particle configurations. The composites were fabricated using stir casting and evaluated for microstructure, hardness, wear behavior, and density. Hardness and strength increased compared to unreinforced alloy, with triple particle composite exhibiting the highest values. Wear resistance was highest for dual particle composite. Density measurements found good casting quality with no porosity.
EFFECT OF ANTIMONY ADDITION RELATIVE TO MICROSTRUCTURE AND MECHANICAL PROPERT...Rautomead Limited
It is well documented that the addition of antimony in pure lead increases tensile strength and reduced elongation. The goal of the present work is to identify the cause of these phenomena by investigation of the effects of the addition of Sb (1.25%) on the structure of pure continuously cast lead and lead alloy rods. The microstructure and morphology of both pure lead and lead 1.25% antimony were examined by digital optical microscope and scanning electron microscope respectively. Energy Dispersive X-ray Spectroscopy (EDX) was used to identify alloying elements. The results showed that the effect of additions of antimony on mechanical properties of lead-antimony alloys is mainly due to the solid solubility of the antimony element. Homogenized distribution of the antimony results in a decrease in the grain size of the pure lead. These smaller grains mean higher strength so long as there is a homogeneous grain structure
This document lists the names of five Dutch businesses: a bakery located at a gas station in Purmerend, a gas station in Purmerend, a gas depot in Amsterdam, a gas station in Koog aan de Zaan, and the transportation company Vos Transport.
This document outlines a course map for mathematics courses, including prerequisites, developmental courses, college-level introductory courses, precalculus sequences, advanced courses, special placements, honors courses, and online homework systems. It provides information on placement into courses based on Combined CPT and SAT math scores and Regents exam scores. It also lists faculty web pages and resources available in the virtual learning commons.
Estefania conducted a survey of her classmates about their favorite music genres. She asked them to select from a list of genres which one fits them best. The results were graphed in a bar chart showing that Reggae was the most popular genre among her classmates with 11 students selecting it, followed by Rock with 9 students and Dubstep also with 9 students.
Sellick Partnership is a recruitment agency that focuses on placing temporary, contract, and permanent legal staff across the UK. They pride themselves on their highly consultative approach and have built strong relationships with 88% of clients returning repeatedly. The agency works to exceed expectations by recognizing individual goals and placing candidates across public, private, and not-for-profit sectors in various legal roles. Testimonials praise their understanding of the legal market and ability to find good matches for clients' needs.
The document lists various World Heritage Sites from different countries around the world. It includes notable landmarks, parks, cities, and other cultural sites that have been designated by UNESCO as being of outstanding universal value. Examples range from the Pyramids of Egypt and the Grand Canyon in the US to the Mzab Valley in Algeria and the Skogskyrkogarde Cemetery in Sweden.
Risk-benefit analysis compares the risks of a situation to its benefits. People accept a certain amount of risk in their daily lives if they feel in control of the situation and can gain some benefit. For example, most people accept the risks of driving because they feel in control of their vehicle. However, when exposed to involuntary risks outside of their control, people's primary goal becomes risk aversion and they require risks to be much smaller. Risk can be viewed differently depending on one's perspective, such as a statistical, projected, or perceived view of risk.
The document provides information about live fashion shows being streamed from Milan, Italy on the blog Macha & Charly. It lists shows from several designers including Marni, Missoni, Trussardi, Dolce & Gabbana, and Salvatore Ferragamo. Viewers can watch live streams of the shows at specific times on February 26.
The document contains various charts and graphs showing data related to music preferences, factory production and scrap rates, education levels and income, monthly expenses, grain and fast food sales, city populations, Red Cross expenses over time, a running workout program, relationship between study time and exam grades, and average monthly temperatures in Chico, California. The charts present numerical and statistical data across various topics providing an overview of trends, comparisons, and relationships within the data.
The document discusses the benefits of exercise for mental health. Regular physical activity can help reduce anxiety and depression and improve mood and cognitive function. Exercise causes chemical changes in the brain that may help protect against mental illness and improve symptoms.
Though small in size, Jamaican culture has had a significant global influence through the development and spread of musical genres like reggae, ska, mento, rocksteady, dub, dancehall and ragga. Reggae in particular influenced the development of punk rock and American rap music, sharing African roots. Internationally renowned reggae artist Bob Marley was Jamaican. Famous Jamaican artists include Bunny Wailer, Peter Tosh, Jimmy Cliff, Dennis Brown, and Shaggy. Traditional Jamaican foods include bammy, bulla, and bun. Popular dances include Myal Maroon, Kumina, Revival and Rastafari. Picturesque Jamaican parishes to visit include Portland, St
Disgrifad o Wasanaeth Cyfieithu Llywodraeth Cymru a'i gronfa ddata terminoleg, TermCymru.
A description of the Welsh Government's Translation Service and its terminology database, TermCymru.
World of Learning: Coaching to embed learning & unleash a collaborative culture by Kate Cooper MBA, BSc, MEd, FInstLM, Senior Advisor: Leadership & Management Development at the Institute of Leadership & Management (ILM)
NetApp Filer auditing is indispensable to data protection, enforcement of internal controls and adherence to external regulations, for those organizations that use NetApp Filer appliances. NetApp monitoring and auditing changes in files, folders, and permissions help tighten security and ensure compliance. Learn how to best go about NetApp Filer auditing, what features are required and how the whole process can be approached.
LEY FUNDAMENTAL DE LA EDUCACIÓN (Honduras 2012)Percy Lopez
La Unión Europea ha propuesto un nuevo paquete de sanciones contra Rusia que incluye un embargo al petróleo. El embargo prohibiría las importaciones de petróleo ruso por mar y por oleoducto, aunque se concederían exenciones temporales a Hungría y Eslovaquia. El objetivo es aumentar la presión económica sobre Rusia para que ponga fin a su invasión de Ucrania.
Om Xpress Print Pack Private Limited is a private limited company established in 2011 and located in Hyderabad, Andhra Pradesh. It manufactures and supplies various printing and packaging products. The company has 15 permanent employees and manufactures products like cartons, packaging items, labels, and printing services. It has two owners, Mr. Narender Kumbala and Mr. Nagender, who each own 50% of the company. Site visits confirmed the company has offices and a factory in urban Hyderabad locations with adequate infrastructure and facilities.
International Journal of Engineering Research and DevelopmentIJERD Editor
The document studies the corrosion process of a Ni-Cr-Mo alloy used in dental prostheses. Electrochemical tests were conducted on samples of the alloy in NaCl solution, and the surface was analyzed at different points on the polarization curve. The results showed the alloy initially forms a protective oxide layer but undergoes transpassivation and intergranular corrosion at higher potentials, with preferential dissolution of regions lower in molybdenum.
nanostructured high strength Mo alloy with unprecented tensile ductility..pptxRishikeshrishi7
This document describes experiments conducted to develop nanostructured molybdenum alloys with improved tensile ductility. Two processing routes were used: liquid-solid doping and a novel liquid-liquid mixing technique. The liquid-liquid technique produced a nanostructured alloy with grain sizes under 500nm and uniformly distributed nanoscale oxide particles. This nanostructured alloy demonstrated unprecedented tensile ductility with 37.5% elongation to failure, over twice as ductile as conventionally processed alloys. The uniform intragranular nanoparticles were able to generate and store dislocations without cracking, leading to the improved ductility.
Study on hardening mechanisms in aluminium alloysIJERA Editor
The Al-Zn-Mg alloys are most commonly used age-hardenable aluminium alloys. The hardening mechanism is
further enhanced in addition of Sc. Sc additions to aluminium alloys are more promising. Due to the
heterogeneous distribution of nano-sized Al3Sc precipitates hardening effect can be accelerated. Mainly,
highlight on hardening mechanism in Al-Zn-Mg alloys with Sc effect is to study. In addition, several
characterisations have been done to age-hardening measurements at elevated temperatures from 120oC to 180
oC. The ageing kinetics has also been calculated from Arrhenius equation. Furthermore, friction stir processing
(FSP) can be introduced to surface modification process and hardened the cast aluminium alloys. In this study,
hardening mechanism can be evaluated by Vicker’s hardness measurement and mechanical testing is present
task.
Fundamentals, synthesis and applications of Al2O3-ZrO2 compositesTANDRA MOHANTA
When the word “Ceramic” comes to our mind, we usually associate them with plates, saucers, cups and mugs. But, the word “Ceramic” encompasses more than just the word “plates” or “saucers”. Indeed, ceramic materials are hard and inherently brittle, but this is just the tip of the iceberg. They have multifarious properties and have acquired a status of high technical importance in the field of scientific research. Ceramics are the soul of the modern day’s structural applications owing to their high mechanical and thermal stability under different challenging conditions. They exhibit remarkable properties such as high hardness, high wear resistance, high corrosion resistance, high elastic modulus, high melting point and the ability to retain high strength at elevated temperatures. Alumina (Al2O3) is one such remarkable ceramic material known for its unique optical, mechanical and electrical properties. But the brittle nature of Al2O3 limits its use in certain engineering applications. Therefore, the strength of Al2O3 and Al2O3- based ceramics can be enhanced by tailoring the microstructural design through the application of strategic techniques that may involve secondary phase particle inclusion (such as Zirconia, ZrO2)
This document summarizes a study on the effect of chromium content on the microstructure and wear resistance of Fe-Cr-C hard facing layers. Hard facing layers containing various amounts of chromium were deposited on mild steel using shielded metal arc welding. Testing found that microstructure consisted of primary (Cr, Fe)7C3 carbides and eutectic phases. Higher chromium content refined the carbides. Wear resistance testing found that higher chromium, carbon, and silicon content resulted in higher hardness and less wear. Electrode I, with higher amounts of these elements, exhibited less wear than Electrode II. In conclusion, chromium content significantly affects microstructure and wear resistance, with higher chromium improving hardness and wear performance of Fe
The document analyzes the microhardness of Al-8Mg alloys after deformation and heat treatment. Cylindrical samples of the alloy were upset to 40% reduction and then heat treated at temperatures from 200 to 4500C. Microhardness measurements along the rolling direction found that homogenized alloy structures exhibited more uniform and higher hardness than as-cast structures. Upsetting and heat treatment enhanced structural uniformity and decreased average hardness with increasing temperature, due to the formation of new strain-free grains and grain growth. A mathematical model was developed to design deformation and heat treatment cycles to achieve desired hardness.
The document summarizes a research project examining a hybrid metal matrix composite combining alumina, zirconia, and titanium. The objectives are to determine an optimal composition, sintering temperature, and mechanical properties including strength, hardness, wear resistance, and temperature resistance. Samples will be prepared by ball milling and pressing the materials, then sintered and tested using water jet machining to determine removal rate, grain structure changes, and surface roughness under different parameters. The project aims to develop a material suitable for applications in nuclear reactors, turbine blades, and advanced engines. Testing will take place at VB Ceramics in Chennai, India.
Effect of dilution on microstructure and hardness of a nickel-base hardfacing...RAMASUBBU VELAYUTHAM
1) The document examines the effect of dilution on the microstructure and hardness of a nickel-base hardfacing alloy deposited on an austenitic stainless steel substrate.
2) Electron probe microanalysis revealed considerable dilution of the hardfacing alloy by the substrate material within the first 2.5mm of the deposit, altering the chemistry, microstructure, and decreasing the hardness in this region.
3) Beyond 2.5mm from the interface, the hardness increases to levels comparable to the undiluted alloy as subsequent deposit layers approach, due to decreasing dilution effects farther from the substrate.
1) The study investigated the microstructure and mechanical properties of continuously cast iron products under different casting conditions and chemical compositions.
2) Key findings were that tensile strength, hardness, and pearlite content increased with higher additions of Cr, Cu, Sb and lower carbon equivalent. Higher Si/C ratio and lower solidification rate also decreased the zone of interdendritic graphite.
3) A structural nomograph was developed to show the effects of solidification rate and chemical composition on the microstructure of continuously cast iron.
Effects of Different Parameters on Molybdenum Concentration in Zn MO Mn Alloyijtsrd
Molybdenum is an active metal possessing high degree of corrosion resistance, hardness, high conduction along with magnetic properties. Alloy containing Zinc, Molybdenum and Manganese have been studied in this paper. The change in properties due to change in temperature, pH and current density, duration of deposition and concentration of Molybdenum in electrolytic solution were the basis of experiments conducted in this paper. The electrolytic concentration and current density produce complimentary effects to a large extent. Effect of various parameters specified above on the concentration of Molybdenum in Zn Mn MO alloy have been studied in this paper. Renu Rastogi "Effects of Different Parameters on Molybdenum Concentration in Zn-MO-Mn Alloy" Published in International Journal of Trend in Scientific Research and Development (ijtsrd), ISSN: 2456-6470, Volume-7 | Issue-3 , June 2023, URL: https://www.ijtsrd.com.com/papers/ijtsrd57394.pdf Paper URL: https://www.ijtsrd.com.com/chemistry/physical-chemistry/57394/effects-of-different-parameters-on-molybdenum-concentration-in-znmomn-alloy/renu-rastogi
IRJET - Fabrication of Magnesium Metal Matrix Composites Reinforced with Fly ...IRJET Journal
This document discusses the fabrication of magnesium metal matrix composites reinforced with fly ash cenospheres. Fly ash cenospheres are a lightweight and low-cost material that can improve the mechanical properties of magnesium composites. The document describes a process of stir casting to mix molten magnesium with 5-20% fly ash cenospheres by weight. This results in a magnesium composite with an improved and refined microstructure, higher hardness, and increased tensile strength compared to magnesium alone. Experimental tests are used to evaluate the mechanical properties and microstructure of the fabricated magnesium composites reinforced with fly ash cenospheres.
Glass polyalkenoate cements (GPCs) are important dental materials that chemically bond to teeth. This study investigated modifying GPCs by adding montmorillonite clay (MMT) to improve their compressive strength and altering their glass composition to change their setting reaction kinetics. FTIR analysis showed MMT addition increased COO-M+ peak intensity over time, indicating improved crosslinking. Compressive strength testing found MMT increased strengths for both glass compositions. The glass with sodium showed slower setting than the sodium-free glass based on weaker COO-M+ peaks and shoulder peaks over time. This study demonstrated methods to optimize GPC properties through additive reinforcement and glass composition tuning.
International Journal of Engineering Research and Applications (IJERA) is an open access online peer reviewed international journal that publishes research and review articles in the fields of Computer Science, Neural Networks, Electrical Engineering, Software Engineering, Information Technology, Mechanical Engineering, Chemical Engineering, Plastic Engineering, Food Technology, Textile Engineering, Nano Technology & science, Power Electronics, Electronics & Communication Engineering, Computational mathematics, Image processing, Civil Engineering, Structural Engineering, Environmental Engineering, VLSI Testing & Low Power VLSI Design etc.
Influence of volume fraction, size, cracking, clustering of particulates and ...eSAT Journals
Abstract
The objective of this study is to examine the influence of volume fraction, size of particulates, formation of precipitates at the
matrix/particle interface, particle cracking, voids/porosity, and clustering of particulates on the strength and stiffness of
6063/SiCp metal matrix composites. Tensile strength and stiffness increase with an increase in the volume fraction of SiC
particulates. The tensile strength and stiffness decrease with increase in size of the particulates, presence of porosity, clustering,
and particle cracking. Formation of particulate clusters is more prominent in the composites having very small-reinforced
particulates. Mg2Si compound is likely to precipitate at the matrix/particle interfaces of 6063/SiC composite.
Keywords: 6063, SiC, clustering, cracking, porosity, clustering
1) A low carbon steel sample with dispersed cementite particles was subjected to warm torsion tests at 685°C to induce deformation in the ferrite phase.
2) The deformation generated defects that acted as nucleation sites for ultrafine ferrite grains less than 1 μm in size, through continuous dynamic recrystallization.
3) Electron backscatter diffraction analysis revealed the final microstructure consisted of ultrafine grains separated by high angle boundaries, showing cementite precipitation and ferrite recrystallization led to intense grain refinement during subcritical deformation.
Novel computing technologies that imitate the principles of biological neural systems may offer low power consumption along with distinct cognitive and learning advantages [1], [2]. The development of reliable memristive devices capable of storing multiple states of information has opened up new applications such as neuromorphic circuits and adaptive systems [3], [4]. At the same time, the explosive growth of the printed electronics industry has expedited the search for advanced memory materials suitable for manufacturing flexible devices [5].
Improving the properties of Ni-Based Alloys by Co AdditionIRJET Journal
1) The document discusses improving the properties of nickel-based alloys through the addition of cobalt.
2) Cobalt addition leads to grain refinement in the alloys, which influences both microstructure and corrosion resistance. Finer grain size improves hardness.
3) Samples of Ni-5Cr-5Al-xCo (where x is the cobalt content from 0-30%) were produced by vacuum arc melting and characterized through XRD, optical microscopy, and Vickers hardness testing.
4) Results showed that increasing the cobalt content refined grain size and improved hardness, while also enhancing corrosion resistance properties over the substrate material alone.
Effect of Nanophase on the Nucleation of Intragranular Ferrite in Microalloye...Nigel Wang
This document discusses the effect of nanophase precipitates on the nucleation of intragranular ferrite in microalloyed steel. It finds that MnS and MnS+V(C,N) complex precipitates provide nucleation centers for intragranular ferrite, leading to grain refinement. Heavy deformation of austenite at low temperatures increases substructures in austenite, causing V(C,N) nanophase to precipitate at these substructures and pin them. The substructures then transform into ultra-fine ferrite grains. Precipitate sizes of 20-50nm provided the best nucleation for intragranular ferrite.
IMPACT Silver is a pure silver zinc producer with over $260 million in revenue since 2008 and a large 100% owned 210km Mexico land package - 2024 catalysts includes new 14% grade zinc Plomosas mine and 20,000m of fully funded exploration drilling.
Tata Group Dials Taiwan for Its Chipmaking Ambition in Gujarat’s DholeraAvirahi City Dholera
The Tata Group, a titan of Indian industry, is making waves with its advanced talks with Taiwanese chipmakers Powerchip Semiconductor Manufacturing Corporation (PSMC) and UMC Group. The goal? Establishing a cutting-edge semiconductor fabrication unit (fab) in Dholera, Gujarat. This isn’t just any project; it’s a potential game changer for India’s chipmaking aspirations and a boon for investors seeking promising residential projects in dholera sir.
Visit : https://www.avirahi.com/blog/tata-group-dials-taiwan-for-its-chipmaking-ambition-in-gujarats-dholera/
Discover timeless style with the 2022 Vintage Roman Numerals Men's Ring. Crafted from premium stainless steel, this 6mm wide ring embodies elegance and durability. Perfect as a gift, it seamlessly blends classic Roman numeral detailing with modern sophistication, making it an ideal accessory for any occasion.
https://rb.gy/usj1a2
How MJ Global Leads the Packaging Industry.pdfMJ Global
MJ Global's success in staying ahead of the curve in the packaging industry is a testament to its dedication to innovation, sustainability, and customer-centricity. By embracing technological advancements, leading in eco-friendly solutions, collaborating with industry leaders, and adapting to evolving consumer preferences, MJ Global continues to set new standards in the packaging sector.
Top mailing list providers in the USA.pptxJeremyPeirce1
Discover the top mailing list providers in the USA, offering targeted lists, segmentation, and analytics to optimize your marketing campaigns and drive engagement.
Storytelling is an incredibly valuable tool to share data and information. To get the most impact from stories there are a number of key ingredients. These are based on science and human nature. Using these elements in a story you can deliver information impactfully, ensure action and drive change.
At Techbox Square, in Singapore, we're not just creative web designers and developers, we're the driving force behind your brand identity. Contact us today.
At Techbox Square, in Singapore, we're not just creative web designers and developers, we're the driving force behind your brand identity. Contact us today.
Taurus Zodiac Sign: Unveiling the Traits, Dates, and Horoscope Insights of th...my Pandit
Dive into the steadfast world of the Taurus Zodiac Sign. Discover the grounded, stable, and logical nature of Taurus individuals, and explore their key personality traits, important dates, and horoscope insights. Learn how the determination and patience of the Taurus sign make them the rock-steady achievers and anchors of the zodiac.
Part 2 Deep Dive: Navigating the 2024 Slowdownjeffkluth1
Introduction
The global retail industry has weathered numerous storms, with the financial crisis of 2008 serving as a poignant reminder of the sector's resilience and adaptability. However, as we navigate the complex landscape of 2024, retailers face a unique set of challenges that demand innovative strategies and a fundamental shift in mindset. This white paper contrasts the impact of the 2008 recession on the retail sector with the current headwinds retailers are grappling with, while offering a comprehensive roadmap for success in this new paradigm.
Building Your Employer Brand with Social MediaLuanWise
Presented at The Global HR Summit, 6th June 2024
In this keynote, Luan Wise will provide invaluable insights to elevate your employer brand on social media platforms including LinkedIn, Facebook, Instagram, X (formerly Twitter) and TikTok. You'll learn how compelling content can authentically showcase your company culture, values, and employee experiences to support your talent acquisition and retention objectives. Additionally, you'll understand the power of employee advocacy to amplify reach and engagement – helping to position your organization as an employer of choice in today's competitive talent landscape.
buy old yahoo accounts buy yahoo accountsSusan Laney
As a business owner, I understand the importance of having a strong online presence and leveraging various digital platforms to reach and engage with your target audience. One often overlooked yet highly valuable asset in this regard is the humble Yahoo account. While many may perceive Yahoo as a relic of the past, the truth is that these accounts still hold immense potential for businesses of all sizes.
1. to be submitted at the 2011 International Symposium on Rhenium held in July 4-8, 2011, Moscow, Russia
RHE IUM EFFECT I MOLYBDE UM-RHE IUM WELDS
F. Morito1, M. I. Danylenko and A. V. Krajnikov.
Institute for Problems of Materials Science (3, Krzhizhanivsky Street, 03680, Kiev, Ukraine)
1
MSF Laboratory (4-20-12, Keyakidai, Moriya, 302-0128, Japan)
Keywords: rhenium effect, Mo-Re alloys, electron-beam welds, sigma-phase, neutron
irradiation, radiarion-induced strengthening
Abstract: << MoRe_Report_Dec1_2010 by Sasha>>
This work analyses several Mo-Re alloys and welds with the Re content 0-50% in as-received
state and after electron beam welding and/or radiation treatment. The mechanical properties
and microstructure of Mo-Re welds are examined focusing on the effect of Re concentration.
Phase stability, microstructural changes and impurity redistribution are studied for better
understanding and predicting the long-term performance of Mo-Re alloys at high
temperatures and/or high neutron fluences.
In particular, a strategy of welding of Mo-Re alloys is discussed with emphasis on the
sensitivity of alloys to pre-weld heatings and on the development of post-weld treatments,
such as warm rolling and annealing, to provide optimal phase composition. Grain refinement
during directional solidification after welding, ductility improvement and fracture mode
change from intergranular to transgranular one are clearly observed with an increase of Re
content.
Effect of neutron irradiation on the strength of Mo-Re welds is studied for a wide temperature
range. Mo-Re welds exhibit a large radiation-induced strengthening. At room temperature, the
strengthening effect is rather limited and unstable because of lack of ductility. The
strengthening becomes strongly pronounced at high temperatures. Damaging effect of
neutrons at high temperatures is shown to be smaller than that at low temperatures.
Intensification of homogeneous nucleation of Re-rich sigma phases in all studied Mo-Re
alloys is observed after high temperature neutron irradiation. As a result, all parts of as-
irradiated welds display approximately same level of strength.
High-temperature annealings with different heating/cooling rates have been used to simulate
thermal conditions in different welding zones. Impurity redistribution in Mo-Re alloys has
been studied by surface analysis methods. The role of carbon and oxygen segregation as well
as formation of carbides and Re-base phases is discussed to minimise intergranular
embrittlement of welds. [14, Sasha]
1
2. Introduction
Rhenium is widely used to alloys VIA group refractory metals. In particular, the strength and
plasticity, creep resistance, and low temperature ductility of Mo are all improved with
increasing the rhenium content due to the so-called “rhenium effect” [1-5].
Fig. 1 shows change of microhardness as a function of Re content in Mo-Re alloys.
1. Solid solution type Mo-Re alloys
1-1. Solution softening and hardening in Mo-Re alloys
Fig. 1 Hardness of Mo-Re alloys annealed at 1873 K for 3.6 ks.
Fig. 2 Yield stress by bend test vs test temperature in Mo-Re welds.
Open marks denote preweld annealing at 1923 K, 1 h and closed ones postweld annealing at
1923 K, 1 h, respectively. ( ) means brittle fracture before yielding.
2
3. Fig. 2 shows yield stress by bend test vs test temperature in Mo-Re welds. Mo-41Re welds
had much higher yield stress than those of Mo-5Re and Mo-13Re, which failed in a brittle
manner at 77 K. But Mo-41Re welds showed more ductile and farctured after yielding even at
77 K.
Fig. 2 also shows a transition of solution softening by a test temperature. At 300 K, Mo-5
wt.% Re exhibited more solution softening than Mo-13 wt.% Re. However minimum yield
stress moved to Mo-13 wt.% Re from Mo-5 wt.% Re with a decrease of test temperature.
2. Previous report on Re effect
In the VI A group metals, the conditions of a resonance covalent bond are fulfilled in the best
way. A deep minimum corresponds to these metals in the plot of state density at Fermi level
(N(EF)). This kind of electron structure causes the peculisrities of structure and mechanical
properties specific for these metals [1]. (Milman et al)
Rhenium Effect by Korotaev et al [2-4]
1. Significant enhancement of low temperature plasticity
2. Reduction of the temperature of the viscous-brittle transition, Tv.b.
3. Suppression of brittle sliding fracture
4. Upgrading of the weldability of high rhenium alloys
Very interestiing characteristic changes in strength properties such as
5. Solution softening in low-rhenium alloys
6. Plastification and reduction of the temperature of the viscous-brittle transition temperature.
Tv.b.
7. Achievement of a remarkably high strength (σ0.1~ 8-9 x 103 MPa ) after deep deformation
(ε> 99 %) by rolling
8. Extraordinaly pronounced effects of solution hardening in the region T > 0.2 Tmelt
A a result, the phenomenology of the enhancement of the strength and plastic properties and
of the features of the deformation and hardening of transition metal-Re alloys. However,
Physical nature of Rhenium Effect has not been elucidated unambiguously up to the present.
(The subject matter of this work is a critical review of the physical nature of Rhenium Effect
and to elucidate the most probable mechanism for these phenomena.)
1. Y. V. Milman and G. G. Kurdyumova, Rhenium effect on the improving of mechanical
properties in Mo, W, Cr and their alloys (review), Proc. International Symposium on
Rhenium and Rhenium Alloys, B.D. Bryskin, ed. TMS, (1997)717-728
2. A. D. Korotaev, A. N. Tyumentsev and Yu. I. Pochivalovl, The rhenium effect in W- and
Mo-base alloys: The experimental regularities and the physical nature, Proc. International
Symposium on Rhenium and Rhenium Alloys, B.D. Bryskin, ed. TMS, (1997)661-670
3
4. 3. A. D. Korotaev, A. N. Tyumentsev, V. V. Manako and Yu. P. Pinzhun, The solubility of
oxygen in rhenium-alloyed molybdenum, Proc. International Symposium on Rhenium
and Rhenium Alloys, B.D. Bryskin, ed. TMS, (1997)671-680
4. A. N. Tyumentsev, A. D. Korotaev, Yu. P. Pinzhu and V. V. Manako, Dispersion and
substructure hardening of Mo-Re-base alloys, Proc. International Symposium on
Rhenium and Rhenium Alloys, B.D. Bryskin, ed. TMS, (1997)707-716
3. Sasha : In addition to traditional applications, such as heating elements, electron tube
components, etc, Mo-Re alloys are considered as candidate materials for structural
applications for chemicals and energy facilities, including elements of fusion or fast
breeder reactors. Welds are obligatory elements of practically any complex construction
while working conditions are characterized by high temperatures (>1000 K), aggressive
medium (liquid metals) and high neutron fluence (>1021 n/cm2).
Therefore, good weldability, high radiation performance, thermal stability and corrosion
resistance are the key issues for these application fields. Tendency of Mo alloys to embrittle at
low temperatures assumes probable degradation of the mechanical properties either during
welding [5-9] or under irradiation [10-13]. In spite of the fact that significant progress has
been achieved in studying the mechanism of rhenium effect, many details of Mo-Re alloy
behaviour under extreme operating conditions are not studied yet.
Table 1 Chemical content of various Mo-Re alloys (wt.ppm).
Re (%) :
0 2 4 10 13 15 20 25 30 40 41 47 50
ominal
Re (wt%) 0 1.7 3.3 8.8 12.0 15.9 21.4 25.6 31.7 37.0 43.6 47.1 50.1
Re (at%) 0 1.0 1.9 5.1 7.1 9.6 13.2 15.2 20.6 24.8 30.2 33.2 36.0
Al 11 7 9 11 <10 <10 <10 <10 83 <5 <10
Ca 5 4 7 7 <1 <1 <1 <1 14 <1 <1
Cr 9 8 9 9 <5 <5 <5 <5 10 <5 23 <5
Cu <3 <3 <3 <3 <5 <5 <5 <5 <3 <1 <5
Fe 20 50 30 50 60 10 10 10 10 150 38 5 10
Mg 2 2 3 3 <1 <1 <1 1 2 <1 <1
Mn <3 <3 <3 <3 <3 <1 <1 <1 <1 <3 <1 <1
i 5 11 10 13 11 <5 <5 <5 <5 20 <5 <3 <5
Pb <3 <3 <3 <3 <10 <10 <10 <10 <3 <10
Si 30 30 30 60 <10 <10 <10 <10 40 <10 <20 <10
Sn <3 <3 <3 <3 <10 <10 <10 <10 <3 <10 <10
a 1 1 1 1 <1 <1 <1 <1 1 <1
K 1 1 1 1 <1 <1 <1 <1 1 <1
C 5 12 7 4 4 10 10 10 10 12 10 10 <10
6 4 2 1 1 <1 <1 <1 <1 1 <10 6
O 18 23 15 14 20 11 10 7 8 66 <10 12
4
5. 4. Irradiation effect on Mo alloys and welds
4-1. Welds of Mo, TZM and Mo-0.56%Nb irradiated to 1017 cm–2 ~ 1020 cm–2 (E> 1 MeV) at
348-1073 K6 (irradiation by JRR-2 and JRR-4 at JAERI).[5]
I. Tensile properties
Mo and TZM, irradiated to 1.2 x 1024 n/m2 at 1073 K (1.2 × 1020 cm–2 (E> 1 MeV))
Fig.3. Tensile properties as a function of test temperature. (a) Tensile stress and (b) Total
elongation in as-welded PM Mo (▽), postweld annealed PM Mo (○), postweld carburized
PM Mo (□), postweld annealed TZM (△) and postweld annealed Mo-0.56 wt.% Nb (◇).
5
6. Fig. 4. Yield stress (△), tensile stress (○) and total elongation (□) of (a) as-welded PM Mo
and (b) postweld annealed TZM irradiated to 1.2 x 1024 m-2 at 1073 K. Closed marks denote
to post-irradiation annealing at 1273 K for 1 h.
For comparison,
PM Mo recrystallized at 1523 K for 1 h and irradiated to 1.3 x 1022 n/cm2 at LT
(Kazaakov & Chakin, 1993)
800
600 YS, Unirrdiated
YS, Irradiated
YS, MPa
400
200
Ef , Unirrdiated
0 Euni , Unirrdiated
50 Ef , Irradiated
40
Euni , Irradiated
30
E, %
20
10
0
300 400 500
T test
, K
Fig. 5. Mechanical properties of PM Mo (recrystallized at 1523 K, 1 h) tensile tested at 300 K,
Blue marks for unirradiated and red marks for irradiated to 1.3 x 10 22 n/cm2 at LT.
6
7. Mo-0.56%Nb, irradiated to 6.0 x 1023 n/m2 at 1073 K (6.0 × 1019 cm–2 (E> 1 MeV))
Total elongation <Tensile test at LT, RT & HT>
Mo-0.56%Nb: BM annealed at 1423K, 1h, 181K
Mo-0.56%Nb: as-welded <Ef~>2% limited to WM and HAZ rather ductile> 235K
Mo-0.56%Nb: postweld annealed at 1673K, 1h, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
<Ef~>20% ductile>
Mo-0.56%Nb: as-welded & irradiated, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
Mo-0.56%Nb: postweld annealed & irradiated, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
Embrittlement due to irradiation was not so significant at RT in the case of Mo-0.56%Nb !!
Fig. 6. Total elongation <Tensile test at LT, RT & HT>
(△) Mo-0.56%Nb: BM annealed at 1423K, 1h, 181K
(△) Mo-0.56%Nb: as-welded <Ef~>2% limited to WM and HAZ rather ductile>
235K
(▽) Mo-0.56%Nb: postweld annealed at 1673K, 1h, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
<Ef~>20% ductile>
7
8. (□) Mo-0.56%Nb: as-welded & irradiated, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
(○) Mo-0.56%Nb: postweld annealed & irradiated, 1073K, 6.0 × 1019 cm–2 (E> 1 MeV)
443K
Embrittlement due to irradiation was not so significant at RT in the case of Mo-0.56%Nb !!
Mo-0.56%Nb
Neutron irradiated to 6.0 x 1023 n/m2 at 1073 K (6.0 × 1019 cm–2 (E> 1 MeV) at 1073 K).
Summary:
We examined mechanical properties of electron-beam welds of Mo and its alloys, TZM and
Mo-0.56wt.% Nb, for nuclear applications. The main results are as follows.
(1) It was shown that mechanical properties of Mo and its alloys were generally degraded by
electron-beam welding and further by neutron irradiation.
(2) Addition of carbon was effective to suppress intergranular embrittlement which was
caused by electron-beam welding and neutron irradiation. It is considered that segregation of
carbon and precipitation of carbides enhanced the intergranular cohesion so that considerable
strength and ductility was maintained.
(3) TZM showed higher strength at high temperatures, but it seemed unavoidable to improve
lower bend ductility especially in the case of neutron irradiation to 1.2 x 1024 n/m2 at 1073 K.
(4) The embrittlement of Mo-0.56wt.% Nb was not so significant at room temperature under
the irradiation to 6.0 x 1023 n/m2 at 1073 K. It is considered that good mechanical properties
of the unirradiated weld of Mo-0.56wt.% Nb were maintained in this case.
Welds of PM-Mo and TZM, irradiated to 1.2 x 1024 n/m2 at 1073 K (1.2 × 1020 n/cm–2 (E>
1 MeV)), F. Morito and K. Shiraishi, (1991)[5]
PM Mo recrystallized at 1523 K for 1 h and irradiated to 1.3 x 1026 n/m2 at LT (1.3 x 1022
n/cm2 at LT), (Kazaakov & Chakin, 1993)
Welds of Mo-0.56wt.% Nb, irradiated to 6.0 x 1023 n/m2 at 1073 K (6.0 × 1019 n/cm–2 (E>
1 MeV)), F. Morito and K. Shiraishi, (1991) )[5]
******************** Attention between Fluences *******************************
1. RIAR : Fig. X Mechanical properties of PM Mo (recrystallized at 1523 K, 1 h) tensile
tested at 300 K, Blue marks for unirradiated and red marks for irradiated to 1.3 x 10 26 m-2
at LT, 1.3 x 10 22 n/cm2 at LT.
2. Mo and TZM, irradiated to 1.2 x 1024 m-2 at 1073 K (1.2 × 1020 cm–2 (E> 1 MeV))
3. Mo-0.56%Nb: postweld annealed at 1673K, 1h, 6.0 x 1023 m-2 at 1073 K 1073K, 6.0 ×
1019 cm–2 (E> 1 MeV)
8
9. 2. RIAR (SM reactor)
2-a LT irradiation : Mo-15Re、20Re、30Re、41Re at 393-433 K to 3.6 - 6.0 × 1025 m–2 (E>
0.1 MeV)7, 8 , 3.6 - 6.0 × 1021 cm–2 (E> 0.1 MeV)7, 8.
2-b HT irradiation : Mo-15Re、20Re、30Re、41Re、50Re at 1023-1073 K to 5.5 - 7.3 ×
1025 m–2 (E> 0.1 MeV)8, 9, 5.5 - 7.3 × 1021 cm–2 (E> 0.1 MeV)8, 9.
[5] F. Morito and K. Shiraishi, Journal of Nuclear Materials, 179, (1991) 592-595.
[6] V.P. Chakin, F. Morito, V.A. Kazakov, Yu.D. Goncharenko and Z.E. Ostrovsky, Journal
of Nuclear Materials, 258-263 (1998) 883-888.
[7] F. Morito, V.P. Chakin, H. Saito, N.I. Danylenko and A.V. Krajnikov, Proc. 17th
International Plansee Seminar, P. Rhoedhammer et al. (Eds.), Reutte/Tirol, vol. 1,
(2009) RM63.
[8] F. Morito , V. P. Chakin, M. I. Danylenko and A. V. Krajnikov, J. Nuc. Mater.,
**(2010)***
III. Irradiated Mo-Re welds at HT 7, 8 <HT irradiation>
20
T = 3 0 0 K
Unirradiated, SR
Unirradiated, Rec
Elongation, %
Irradiated, SR
Irradiated, Rec
10
0
0 10 20 30 40
Re content, %
Fig. 7. Fracture elongation tested at 300 K in Mo-Re welds. (Open mark=Recrystallized
(Rec), Closed mark=Stress-relieved (SR). : unirradiated, ----- : irradiated).
9
10. T = 1 0 2 3 K /1 0 7 3 K
30
Elongation, %
20
10 Unirradiated, SR
Unirradiated, Rec
Irradiated, SR
Irradiated, Rec
0
0 10 20 30 40
Re content, %
Fig. 8. Fracture elongation tested at 1023 K for unirradiated and 1073 K for irradiated in Mo-
Re welds. (Open mark=Recrystallized (Rec), Closed mark=Stress-relieved (SR). :
unirradiated, ----- : irradiated).
10
11. (a)
1600
Unirradiated, SR
1400
Unirradiated, Rec
Tensile strength, MPa
1200 Irradiated, SR
Irradiated, Rec
1000
800
600
400
200
0
0 10 20 30 40 50
Re content, %
(b)
1600
Unirradiated, SR
1400 Unirradiated, Rec
Irradiated, SR
Tensile strength, MPa
1200 Irradiated, Rec
1000
800
600
400
200
0
0 10 20 30 40 50
Re content, %
Fig. 9. Tensile strength tested (a) at 300 K and (b) at 1023 K for unirradiated and 1073 K for
irradiated in Mo-Re welds. (Open mark=Recrystallized (Rec), Closed mark=Stress-relieved
(SR). : unirradiated, ----- : irradiated).
1400 Unirrad., SR, BM
Unirrad., Rec, BM
Irrad., SR, WM
1200 Irrad., SR, HAZ
Irrad., SR, BM
Irrad., Rec, WM
Microhardness
1000 Irrad., Rec, HAZ
Irrad., Rec, BM
800
600
400
200
0
0 10 20 30 40 50
Re content, %
Fig. 10. Hardness at 300 K in Mo-Re welds. (Open mark=Recrystallized (Rec), Closed
mark=Stress-relieved (SR). : unirradiated, ----- : irradiated).
11
12. Fig. 11. Density change (∆d/dini) in Мо-Re welds irradiated at Тirr = 1023-1073 K. ( ∆d=dirr -
dini , dini : Density before irradiation, dirr : Density after irradiation).
(a) Unirrad. BM, (b) Unirrad. WM
Fig. 12. Unirradiated microstructutre of Mo-Re welds (postweld annealed at 1673 K, 1 h) : (a)
Mo-15Re: Unirrad. BM, postweld, (b) Mo-15Re: Unirrad. WM.
In the initial state of the Mo-Re welds, for example, only dislocations, dislocation networks
and dislocation tangles with rather low density are seen (Fig. 12-11 (a ) and (b)).
12
14. (a) (b) (c)
40 µm
(d) (e)
Fig. 14. Fracture surfaces of postweld recrystallized Mo-Re welds irradiated at Тirr = 1023-
1073 K. (a) Mo-15Re, (b) Mo-20Re, ( c) Mo-30Re, (d) Mo-41Re, (e) Mo-50Re.
14
15. 4 µm 4 µm
a b
Particles of
second
phase
4 µm 4 µm
c d
Fig. 15. Fracture surface of Мо-Re welds irradiated at Тirr = 1023-1073 K after tensile test at
room temperature:
a) Mo-15Re; 1673 K, 1h; BM b) Mo-20Re; 1673 K, 1h; WM
c) Mo-30Re; 1673 K, 1h; BM d) Mo-41Re; 1673 K, 1h; BM
15
16. 8 µm
40 µm
a
8 µm
40 µm
b
8 µm
40 µm
c
Fig. 16. Metallography of Mo-20Re weld; 1673 K, 1h:
a) BM
b) HAZ
c) WM
16
17. 90 nm
a
90 nm
b
150 nm
c
Fig. 17. TEM microstructure of Мо-Re welds irradiated at Тirr = 1023-1073 K.
a) particles of second phase, Mo-15Re; 1673 K, 1h;
b) particles of second phase, Mo-41Re; 1673 K, 1h;
c) grain boundary, Mo-41Re; 1673 K, 1h
17
18. 1000
800
600
Hv
400
200
0
0 10 20 30 40 50
Re content, %
Fig. 18. Microhardness of Mo-Re welds (postweld annealed at 1173 K, 1 h) :
Irradiation at Тirr = 1023-1073 K up to fluence F=(5.5-7.3)×1021 cm-2 (Е>0.1 MeV).
- initial state ○ - irradiated
3. Results <HT irradiation>
The tensile strength of both irradiated and unirradiated welds is shown in Fig. 1a and Fig. 1b
as a function of Re content for room temperature and high temperature tests respectively.
Almost all welds failed in a very brittle manner at room temperature. But all the welds
demonstrated adequate ductility with elongation ~20-30% at high temperatures. Although
some variations of strength data were recognized in irradiated samples, tensile strength
generally increased with Re content. After neutron irradiation, Mo-Re welds showed a large
radiation-induced strengthening. At room temperature, the strengthening effect was rather
limited and unstable because of lack of ductility. It appeared in some samples with residual
ductility but was absent in absolutely brittle samples. The strengthening became strongly
pronounced at high temperatures. In particular, tensile strength of all irradiated welds at
1073 K was sufficiently higher than that of unirradiated specimens at 1023 K. For example,
tensile strength of Mo-16Re and Mo-45Re alloys in Rec state increased from 240 to 960 MP
and from 420 to 1250 MPa respectively. The radiation-induced strengthening at high
temperature was estimated to be about 700-800 MPa and rather independent on the Re content.
Microhardness of irradiated and unirradiated welds is shown in Fig. 2. The hardness of all
zones of welds, such as weld metal (WM), heat-affected zone (HAZ) and base metal (BM),
usually increased with the Re content. For any irradiated specimen, the difference in hardness
18
19. between different welded zones was very small, if any. Each zone of all irradiated welds
exhibited a severe radiation-induced hardening compared to that of unirradiated samples. An
increase of the microhardness resulted from high temperature irradiation was approximately
300 MPa for SR welds and varied between 400 and 600 MPa for Rec samples depending on
the Re content. Fig. 3 shows an increase of density (∆d/ dini) in Mo-Re welds after high
temperature irradiation. Density of irradiated welds (dirr = dini+∆d) increased to 3.8-9.1%
compared with their initial density (dini). The value of ∆d/dini is almost constant for Mo-Re
welds with 16-21% Re. Further increase of Re content monotonously weakens the observed
effect of density growth. As shown in Fig. 4, massive secondary phases were recognized as
the form of thin plane particles with 70-160 nm length in all the Mo-Re welds. It indicates
that microstructure reconstruction of irradiated Mo-Re welds is connected with the formation
of secondary phases of much higher density compared with that of unirradiated specimen.
19
20. IV. Irradiated Mo-Re welds at LT 6, 7 <LT irradiation>
XT Legend
B
30 30 C
R
D
20 20
YR
E , %
f
10 10
0 Line 0
0 10 20 30 40
XT
1000
Text
B
C
800 R
D
YL
600 U n ir r a d ia te d
σYS , MPa
Text2
YR
400
Arrow1
Arrow
Ir r a d ia te d
200 Text1
Arrow2 Arrow3
0
0 10 20 30 40
XB
Re content, %
Fig. 19. Result of Mo-Re welds tensile tested at 293 K and 673 K. (a) Total elongation (δtot),
(b) Yield stress (σYS). △:Unirrad. postweld annealed at 1173 K, Ttest = 293 K, ▲:Irrad.
postweld annealed at 1673 K, Ttest = 293 K, ○:Unirrad. postweld annealed at 1673 K, Ttest =
293 K, ●:Irrad. postweld annealed at 1673 K, Ttest = 293 K, ◇:Unirrad. postweld annealed
at 1173 K, Ttest =673 K, 1173 K, ◆:Irrad. postweld annealed at 1173 K, Ttest = 673 K, □:
Unirrad. postweld annealed at 1673 K, Ttest = 673 K, ■:Irrad. postweld annealed at 1673 K,
Ttest = 673 K, br: brittle rupture.
20
21. (a) (b) (c)
Fig. 20. Macrostructure of tensile specimen fractured at WM. (a) Mo-15Re fractured during
disassembling of capsule, (b) Mo-20Re fractured during disassembling of capsule, (c) Mo-
30Re fractured by tensile test at RT.
21
22. (a) (b)
(c) (d)
(e) (f)
Fig. 21. Microstructure of postweld annealed Mo-Re welds irradiated at LT.
(a) Mo-20Re: Irrad. BM, (b) Mo-20Re: Irrad. WM (postweld annealed at 1673 K, 1 h)
(c) Mo-30Re: Irrad. WM, (d) Mo-30Re: Irrad. WM (postweld annealed at 1173 K, 1 h)
(e) Mo-41Re: Irrad. BM, (f) Mo-41Re: Irrad. WM (postweld annealed at 1173 K, 1 h)
In recryatallized Mo-Re welds, only dislocations, dislocation networks and dislocation tangles
with rather low density are seen (Fig. 12-11 (a ) and (b)). Dislocation density in WM was less
than in the BM. So, the dislocation density in BM was 2.9 x 1010 cm-2 and that in WM was 1.9
x 1010 cm-2 for the Mo-15Re weld.
The results of TEM investigations of irradiated Mo-Re welds are presented in Fig. 12-13 (c) -
(f) and in Table 3. Iirradiation leads to the formation of the dislocation loops typical for such
low-temperature irradiation. Their average size is 7.5 ~ 10 nm. Density of dislocation loops
22
23. varied in the range from 4.5 ´ 1015 to 2.6 ´ 1016 cm-3 and decreased with an increase of
rhenium content.
The structure of all irradiated Mo-Re alloys is retained as one phase. The second phase
precipitations, which were remarkably observed in Mo-Re welds irradiated at higher
temperatures [1], were not detected.
Dislocation loop distribution in BM of Mo-41Re welds was extremely irregular, but
dislocation loops were almost absent in WM as in Fig. 12-13 (e), (f). The reason is to be
solved why these phenomena are mainly due to Re effect.
12
10 WM 2
Loop Size / nm
30Re 20Re
1
8 BM 3 4
WM BM
5
BM
6 41Re
4 15 16 17
10 10 10
Loop Density / cm-3
Fig. 22. Dislocation loop density vs size in Mo-Re welds irradiated at LT.
5. Conclusions
1. Irradiation of the tensile specimens and TEM disksof the welds of Mo±alloys with 15%,
20%, 30% and 41%rhenium contents at 120±160°C to the neutron ¯uence of 6.0 x 1021 n/cm2
(E > 0.1 MeV) led to the strong radiation embrittlement. The fracture took place only over the
specimens centre through the weld-fusion zone. With increasing rhenium content the fracture
type changed from the brittle intergranular type to the transgranular one.
23
24. 2. It was shown that with increasing rhenium contentthe dislocation loop density with an
average size of 7.5~10 nm was reduced 4~6 times and in the fusion zone of Mo-41Re welds
were quite absent.
V. Summary <HT irradiation>& <LT irradiation>
Radiation-Induced Segregation, Precipitation, Hardening, Embrittlement, Transmutation
11. RIP
Nucleation sites of σ-phase are considered to be subgrain boundaries consisting of tangled
dislocations, because the number of density of subgrains is changed with thermal treatment.
Consequently it is considered that the number of density of σ-phase precipitations can be
controlled by thermal treatment.
On the other hand, the mean length and the number of density of χ-phase precipitates were not
changed with thermal treatment. This suggests that the nucleation site of χ-phase are
dislocations and dislocation loops formed at the beginning of irradiation ( < 1 dpa ) **.
**. B. N. Singh, J. H. Evans, A. Horsewell, P. Toft and G. V. Muller, J. Nuc. Mater., 258-
263(1998)865
After nucleation of these σ-phase and χ-phase precipitates, the surface of the precipitates acted
as a sink for under size elements such as Re atoms, leading to the growth of the precipitates.
Nelson et al124 : satulated radius and number of density of sphere shaped RIP gamma prime
phase precipitates in Ni-Al alloy -> Fig. 11
12. RIH and RIE by Orowan model126-128 -> Fig.12: Re content dependence of radiation
hardening calculated from results of the microstructural observation. Calculated Hv agreed
with the measurement in the specimens irradiated at 1072 K. In the specimens irradiated at
681 or 874 K, the scatter of the calculation became larger. It is considered because there
would be invisible small defects at lower temperature irradiation.
12*. RIE
For Mo-41Re irradiated at 874 K or below, there were cracks observed around the indentation
after Hv measurements. This embrittlement is thought to be caused by large and hard σ-phase
precipitates. σ-phase has very high HV value of about 1500 (MPa), which is much larger than
that of the matrix, and hence the surface or inside of such hard precipitates would be the
initiation sites of cracks. Thus the formation of large σ-phase ppts led to drastic embrittlement
in the Mo-41Re.
2. χ-phases which are usually close to spheroids by ion irradiation [20]
3. Ageing at 1098 and 1248 K of two-phase Mo-47.5 wt% Re with αMo + σ structure was
recently shown to form χ-phase along grain boundaries [24].
24
25. [24] K.J. Leonard, J.T. Busby and S.J. Zinkle, Journal of Nuclear Materials, 366, (2007) 369-
387
Microstructural and mechanical property changes with aging of Mo–41Re and Mo–
47.5Re alloys
The changes in microstructure and mechanical properties of Mo–41Re and Mo–47.5Re alloys
were investigated following 1100 h thermal aging at 1098, 1248 and 1398 K. The electrical
resistivity, hardness and tensile properties of the alloys were measured both before and after
aging, along with the alloy microstructures though investigation by optical and electron
microscopy techniques.
(1) The Mo–41Re alloy retained a single-phase solid solution microstructure following
1100 h aging at all temperatures, exhibiting no signs of precipitation, despite measurable
changes in resistivity and hardness in the 1098 K aged material.
(2) Annealing Mo–47.5Re for 1 h at 1773 K resulted in a two-phase αMo + σ structure,
(3) with subsequent aging at 1398 K producing a further precipitation of the σ phase along
the grain boundaries. This resulted in increases in resistivity, hardness and tensile strength
with a corresponding reduction in ductility.
(4) Aging Mo–47.5Re at 1098 and 1248 K led to the development of the χ phase along grain
boundaries, resulting in decreased resistivity and increased hardness and tensile strength
while showing no loss in ductility relative to the as-annealed material.
RIT : [25] E.J. Edwards, F.A. Garner and D.S. Gelles, Journal of Nuclear Materials, 375,
(2008) 370-381.
4-1. Mo–41 wt% Re irradiated in the fast flux test facility (FFTF) experienced significant and
non-monotonic changes in density due to radiation-induced segregation, leading to non-
equilibrium phase separation, and progressive transmutation of Re to Os [25].
4-2 irradiation of Mo–41 wt% Re over a range of temperatures (743-1003 K) to 28–96 dpa
produced a high density of thin platelets of a hexagonal close-packed (hcp) phase identified
as a solid solution of Re, Os and possibly a small amount of Mo.
4-2* < Grain boundaries are also enriched with Re to form the hcp phase, but the precipitates
are much bigger and more equiaxed in shape.>
4-3. Although not formed at a lower dose, continued irradiation at 1003 K leads to the co-
formation of late-forming χ-phase, an equilibrium phase that then competes with the pre-
existing hcp phase for rhenium.
4. Discussion <ICFRM-14=JNM2010> 9
In accordance with the phase diagrams [18, 19], formation of σ-phases and χ-phases takes
place at high temperatures in Mo-Re alloys with a high Re content. Formation of secondary
phases under irradiation in solid solution is possible due to radiation-induced segregation of
Re atoms followed by Re enrichment of internal sinks up to solubility limit or even exceeding
it. We already reported that σ-phase was recognized in Mo-50Re alloys and welds [15, 16].
We also showed that thermo-mechanical treatment was much effective to improve mechanical
25
26. properties of Mo-50Re welds by controlling dispersion and size of σ-phase along grain
boundaries and in the matrix [16, 17]. The results obtained here also correspond well with the
previous ones [20-22]. As was shown here, formation of secondary phases is significant and
intensive in Mo-Re welds. Character and rate of phase formation are almost independent on
the Re content as well as on the location within the welded zone. Secondary phases look like
thin plane particles located along some crystallographic planes as shown by TEM. Based on
the particle shape, one may conclude that they are σ-phases rather than χ-phases which are
usually close to spheroids [20]. High intensity of secondary phase formation, homogeneous
distribution of the particles over the bulk, and absence of depleted zones along grain
boundaries indicate that the phases were formed by means of mechanism of homogeneous
nucleation which is based on the radiation-induced separation of atoms in alloys [23]. In this
case, formation of stable nuclei can occur in defect-free areas of welds. In other words,
nucleation occurs homogeneously over the grain bulk and it does not preferentially correlate
with structure defects such as voids, dislocations, grain boundaries and so on. Susceptibility
of Mo and Re atoms to separation under irradiation is high and stability of the formed nuclei
is sufficient to continue growth of particles as a consequence of radiation-induced segregation.
Independence of phase formation rate on the Re content supports our assumption about a very
high intensity of radiation-induced separation of Mo and Re atoms in Mo-Re welds under
neutron irradiation. This eliminates effect of alloy composition on the final microstructure and
leads to formation of practically the same number of secondary phases in the welds in spite of
Re content. Ageing at 1098 and 1248 K of two-phase Mo-47.5 wt% Re with αMo + σ
structure was recently shown to form χ-phase along grain boundaries [24]. Mo–41 wt% Re
irradiated in the fast flux test facility (FFTF) experienced significant and non-monotonic
changes in density due to radiation-induced segregation, leading to non-equilibrium phase
separation, and progressive transmutation of Re to Os [25]. Beginning as a single-phase solid
solution of Re and Mo, irradiation of Mo–41 wt% Re over a range of temperatures (743-
1003 K) to 28–96 dpa produced a high density of thin platelets of a hexagonal close-packed
(hcp) phase identified as a solid solution of Re, Os and possibly a small amount of Mo. These
hcp precipitates are thought to form in the alloy matrix as a consequence of strong radiation-
induced segregation to Frank loops. Grain boundaries are also enriched with Re to form the
hcp phase, but the precipitates are much bigger and more equiaxed in shape. Although not
formed at a lower dose, continued irradiation at 1003 K leads to the co-formation of late-
forming χ-phase, an equilibrium phase that then competes with the pre-existing hcp phase for
rhenium.
After low temperature irradiation, fracture surface is mainly located in WM, because this zone
usually has the lowest strength among other welded zones [7-9].
Mo-Re welds have a tendency to exhibit intergranular embrittlement in alloys with a lower Re
content and under low temperature irradiation.
In contrast to low temperature irradiation, all zones of welds after high temperature irradiation
are characterized by comparable strength level. Thus, fracture at room temperature occurred
at any place of the welds by brittle transgranular cleavage.
Numerous secondary phases were observed at cleavage lines and within matrix. In addition
the number and morphology of these particles were almost independent on the Re content.
The reason of this effect is the same as discussed above.
26
27. Intensive phase formation in Mo-Re welds eliminated any difference in mechanical properties
between WM, HAZ and BM. Mo-Re welds with such a characteristic microstructure still kept
sufficient plasticity at high temperatures. Therefore it is clear that high temperature neutron
irradiation of Mo-Re welds have lesser damaging effect than low temperature irradiation.
As a result, we obtained a very important practical conclusion that weld-fabricated
constructions operating under high temperature radiation do not limit their life because
mechanical properties of welds with WM and HAZ are not worse than those of BM.
Concluding remarks
1. The presence of σ-phases is effective to suppress embrittlement of two-phase precipitated
Mo-Re alloys and welds, controlling their population such as distribution, size and density
combined with thermo-mechanical treatments (TMT). As a result, it is possible to enhance
Re effect keeping lower temperature ductility and higher temperature strength.
2. Weldability was much improved among Mo-Re alloys with higher Re contents, which is
exhibited as significant role by Re effect both in unirradiated and irradiated conditions.
3. Due to irradiation, Mo-Re alloys in solid solution signicantly formed σ-phases. Mo-Re
alloys of two-phase type further enhanced precipitation and growth of σ-phases. With an
increase of irradiation, σ-phases precipitation much increased by promoting radiation-
induced segregation and radiation-induced precipitation.
4. Radiation-induced segregation, radiation-induced precipitation, radiation-induced
hardening was recognized during neutron irradiation of Mo-Re alloys and welds. Among
Mo-Re with higher Re contents, radiation-induced strengthening was considerably
promoted at higher temperature irradiation. But radiation-induced embrittlement at RT
remains to be overcome in the case of lower temperature irradiation less than 400 K.
5. Problems on density increase of Mo-Re welds after irradiation are desirable and raise a
good discussion about Re effect, I think.
27
28. References-x
1. R. EcK, Proc.11th International Plansee Seminar, 1(1985)39
2. G. A. Geach and J. R. Hughes, Proc. 2nd Plansee Seminar, Pergamon Press, London,
(1956)245
3. Von. I. Glass and G. Bohm, Planseeberichte. 10(1962)144
4. A. Lawlay and R. Maddin, Trans. Met. Soc. AIME, 224(1962)573
5. D. L. Davidson and F. R. Brotzen, Acta Met. 18(1970)463
6. W. D. Klopp and W. R. Witzke, Met.Trans. 4 (1973)2006
7. L. B. Lundberg, E. K. Ohriner, S. M. Tuominen, E. P. Whelan and J. A. Shields, Jr.
Physical Metallurgy and Technology of Molybdenum and Its Alloys, Eds. K. H. Miska et al.
AMAX, Ann Arbor, MI, (1985)71
8. J. Wadsworth, C. M. Packer, P. M. Chewey and W. C. Coons, Mater. Sci. Eng.
59(1983)257
9. F. Morito, J. Less-Comm. Met. 146(1989)337
10. F. Morito, Proc. 12th Intern. Plansee Seminar, 1(1989)417
11. F. Morito, J. Phys. IV, 1(1993)553
12. F. Morito, JOM, 45(1993)54
13. F. Morito, Proc. 13th Int. Plansee Seminar, 1(1993)585
14. F. Morito, High Temp. & High Press. 26(1994)101
15. T.B. Massalski, Eds. Alloy Phase Diagrams, vol. 2, ASM International, Metals ParK, OH,
(1986)
16. J. Wadsworth, T. G. Nieh and J. J. Stephens, Scripta Met. 20(1986)637
17. R. EcK, Planseeberichte. 22(1974)165
18. T. Takebe, T. Akiyama, K. Shimatani and M. Endoh, Physical Metallurgy and
Technology of Molybdenum and Its Alloys, Eds. K.H.Miska et al. AMAX,Ann Arbor,MI,
(1985)41
19. C. M. McNally, W. H. Kao and T. G. Nieh, Scripta Met. 22(1988)1847
20. J. Schrank and M. Kuhlein, Refractory and Hard Metals, 6(1987)106
21. F. Morito and K. Shiraishi, J. Nuc. Mat. 179-181(1991)592
22. S. A. Fabritsiev, V. A. Gosudarenkova, V. A. Potapova, V. V. Rybin, L. S. Kosachev, V.
P. Chakin, A. S. Pokrovsky and V. R. Barabash, J.Nuc.Mat. 191-194(1992)426
23. T. Suzuki and I. Mutoh, J. Nuc. Mat. 184(1991)81
28
29. 24. T. Suzuki and I. Mutoh, Proc. Workshop on High Temperature Corrosion of Advanced
Materials and Protective Coatings," Eds. Y. Saito et al. Elsevier Sci. Pub. B. V. ToKyo,
(1992)227
25. T. Flament and J. Sannier, Proc. 4th Intern. Conf. on Liquid Metal Engineering and
Technology, Societe Francaise d'Energie Nucleaire and Commissariat a l'Energie Atomique,
Avingon, France, 2(1988)520/1
26. J. A. Shields Jr, Proc. 1992 Powder Metallurgy World Congress, Metal Powder
Federation, Princeton, NJ, 8(1992)199
27. J. A. Shields Jr, Adv. Mat. Proc. 1421(1992)28
28. A. J. Bryhan, Adv. Mat. Proc. 1431(1993)50
29. F. Morito, J. Nuc. Mat. 165(1989)142
30. F. Morito, J. Mat. Sci. 24(1989)3403
31. F. Morito, Proc.12th International Plansee Seminar'89, 1(1989)313
32. F. Morito, Vacuum, 41(1990)1743
33. F. Morito, Colloque de Physique, C1-51(1990)281
34. F. Morito, Surf. Interf. Analysis, 15(1990)427
35. N. Igata, A. Kohyama and K. Itadani, J. Nuc. Mat. 85-86(1979)895
36. A. Kohyama and N. Igata, J. Nuc. Mat. 122(1984)767
29
30. References-y
1. J. W. Blossom, “Annual Report 1990”, U. S. Department of the Interior, Bureau of Mines,
April 1992
2. J. Wadsworth and J. P. Wittenauer, LLNL Report, 1993
3. 五十嵐廉、まてりあ、41(2002)362
4. S. Primig, H. Leitner, A. Rodriguez-Chavez, H. Clemens, A. Lorich, W. Knabl, R. Stickler,
Proc. 17th International Plansee Seminar, G. Kneringer et al. Eds. Reutte/Tirol, 1(2009)RM15
5. M. Endo, K. Kimura, T. Udagawa and H. Seto, Proc. 12th International Plansee Seminar, G.
Kneringer et al. Eds. Reutte/Tirol, 1(1989)37
6. C. Stallybrasse, G. Leichtfried and A. Kneissl, Proc. 15th International Plansee Seminar, G.
Kneringer et al. Eds. Reutte/Tirol, 1(2001)267
7. 瀧田朋広、五十嵐廉、土肥義治、粉体および粉末冶金、45(1998)969
8. 瀧田朋広、五十嵐廉、馬淵守、中村守、土肥義治、長柄毅、粉体および粉末冶金、
46(1999)1031
9. 瀧田朋広、五十嵐廉、斎藤尚文、中村守、粉体および粉末冶金、46(1999)1261
10. 五十嵐廉、粉体および粉末冶金、49(2002)163
11. Y. Kitsunai, H. Kurishita, M. Narui, H. Kayano, Y. Hiraoka, J. Nuc. Mat. 239(1996)253
12. H. Kurishita, Y. Kitsunai, T, Kuwabara, M. Hasegawa, Y. Hirao Ka, T. Takida and T.
Igarashi, J. Nuc. Mat. 75(1999)594
13. Y. Kitsunai, H. Kurishita, T. Kuwabara, M. Narui, M. Hasegawa, T. Takida and K.
Takebe, J. Nuc. Mat. 346(2005)233
14. H. Kurishita, S. Satou, H. Arakawa, T. Hirai, J. Linke, M. Kawai and N. Yoshida,
Advanced Materials Research, 59(2009)18
15. 藤井忠行、北海道大学学位論文、1984
16. T. Fujii, R. Watanabe , Y. Hiraoka and M. Okada, J. Less-Common Met. 96(1984)297
17. T. Fujii, R. Watanabe , Y. Hiraoka and M. Okada, J. Less-Common Met. 97(1984)163
18. K. Tsuya and N. Aritomi, J. Less-Common Met. , 15(1968)245
19. J. P.Touboul, L. Minel and J. P. Langeron, J. Less-Common Met. 30(1973)279
20. Y. Hiraoka, F, Morito, M. Okada and R. Watanabe, J. Nucl. Mat. 78(1978)192
21. S. Suzuki, H. Matsui and H. Kimura, Mat. Sci. Eng. 47(1981)209
22. D. S. Wilkinson, K. Abiko, N. Thyagarajan and O. P. Pope, Met. Trans. 11A(1980)1827
23. 木村宏, 日本金属学会報, 22(1983)85
30
31. 24. M. P. Seah, Acta Met. 28(1980)955
25. W. Losch, Acta Met. 27(1979)1885
26. C. L. Briant and R. P. Messmer, Phil. Mag. B42(1980)569
27. 小川孝好, 石田洋一, 日本金属学会誌, 43(1979)1048
28. 安彦兼次, 木村宏, 鈴木茂, 鉄と鋼, 69(1983)625
29. M. Oku, S. Suzuki H. Kurishita and H. Yoshinaga, Appl. Surf. Sci. 26(1986)42
30. A. Lawlay, J. Van den Sype and R. Maddin, J. Inst. Metals, 23(1962-63)23
31. D. J. Capp, H. W. Evans and B. L. Eyre, J. Less-Common Met. , 40(1975)9
32. 及川秀男, 材料科学, 20(1984)36
33. L. E. Olds and G. W. P. Rengstorff, J. Metals, 8(1956)150
34. J. B. Brosse, R. Fillet and M. Biscondi, Scripta. Met. 15(1981)619
35. A. Kumar and B. L. Eyre, Proc. Roy. Soc. Lond. A370(1980)431
36. 野田哲二, 貝沼紀夫, 岡田雅年, 日本金属学会誌, 48(1984)604
37. H. Kurishita, H. Yoshinaga, K. Abi Ko, S. Suzuki and H. Kimura, Proc. 4th Int. Symp. on
Grain Boundary Structure and Related Phenomena, Supplement to Trans. JIM, 27(1986)739
38. G. Lorang, These Doctorat d'Etat, Orsay, Dec. 1980
39. G. Lorang, P. Ailloud, L. Debove, J. C. Rouchaud, M. Fedoroff and J. P. Langeron, Z.
Metallkde. 74(1983)458
40. A. Kobylanski et C. Goux, C. R. Acad. Sci. Paris, 272C(1971)1937
41. J. M. Jardin, A. Kobylanski et C. Goux, C. R. Acad. Sci. Paris, 280C(1975)717
42. 栗下裕明, 久芳俊一, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)539
43. 栗下裕明, 大石朗, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)546
44. J. M. Vitek and M. Ruhle, Acta Met. 34(1986)2085
45. A. Kumar and B. L. Eyre, Acta Met. 26(1978)569
46. T. W. Haas and J. T. Grant: Appl. Phys. Let. 16(1970)172
47. J. T. Grant and T. W. Haas, Surf. Sci. 24(1971)332
48. E. Gillet, J. Less-Common Met. , 71(1980)277
49. M. Frorjancic, M. Ruhle and S. L. Saas, Proc. 10th Int. Congr. Electron Microscopy,
2(1982)359
50. J. M. Penisson, M. Bacia and M. Biscondi, Phil. Mag. A, 73(1996)859
51. I. F. Fergson, J. B. Ainscough, D. Morse and A. W. Miller, Nature, 02(1964)1327
52. H. Lux and A. Ignatowicz, Chem. Ber. 101(1968)809
31
32. 53. V. I. Arkharov, V. N. Koney and A. F. Gerasimov, Fiz. Metal. Metalloved. 9(1960)695
54. P. Ettmayer, Monatsh. Chem. 101(1970)127
55. K. Kunimori, T. Kawai, T. Kondow. T. Onishi and K. Tamaru, Surf. Sci. 54(1976)525
56. T. Kawai, K. Kunimori, T. Kondow, T. Onishi and K. Tamaru, Phy. Rev. Let.
33(1974)533
57. H. Mi Ki, K. Kato, A. Kawana, T. Kioka, S. Sugai and K. Kawasaki, Surf. Sci.
161(1985)446
58. A. Ignatiev, F. Jona, D. W. Jepsen and P. M. Marcus, Surf. Sci. 49(1975)189
59. H. Kurishita, H. Yoshinaga, K. Abi Ko, S.Suzuki and H. Kimura, Trans. JIM,
27(1986)739
60. H. Kurishita, O.Tokunaga and H.Yoshinaga, Mater. Trans. JIM, 31(1990)190
61. M. Taheri, Mat. Sci. Eng. 32(1978)221
62. T. Noda and M. Okada, Trans. JIM. 28(1987)517
63. M. K. Miller, E. A. Keni K, M. S. Mousa, K. F. Russel and A. J. Bryhan, Scripta Met.
46(2002)299
64. 斎藤秀雄, 森藤文雄, 鐵と鋼, 89(2003)750
65. F. Morito, N.I. Danylenko, H. Saito and A.V. Krajnikov, Metallic Materials with High
Structural Efficiency, O. N. Senkov, D. B. Miracle and S. A. Firstov, eds. Dordrecht,
Netherlands, Kluwer Academic Publishers, (2004)347
66. 斎藤秀雄, 森藤文雄, 材料工学領域における最新オートラジオグラフィーの解析と
その応用, 編著:斎藤秀雄, うらべ書房, 千葉, (2008)101
67. F. Morito, V. P. Chakin, H. Saito, A. V. Krajnikov and M. I. Danylenko, Proc. 17th
Plansee Seminar, G. Kneringer et al. Eds. Reutte, Tirol, Austria, 1(2009)RM63
32
33. References-a
1. W. N. Platte, Weld. J. 35(1956)369s
2. W. N. Platte, Weld. J. 36(1957)301s
3. M. M. Nerodenko, E. P. Polishchuk and T. D. Galinzovskays, Autom. Weld. 32(1979)39
4. M. M. Nerodenko, E. P. Polishchuk and T. D. Galinzovskays, Autom. Weld. 32(1979)42
5. A. J. Bryhan, Welding Research Council, Bulletin-312, 1986
6. J. L. Jellison, Sandia National Laboratories Report SAND79-0193, (1979)
7. F. Matsuda, M. Ushio, K. Nakata and Y. Edo, Trans. JWRI. 8(1979)217
8. R. EcK, Proc. 11th Intern. Plansee Seminar, 1(1985)39
9. R. Kishore and A. Kumar, J. Nucl. Mat.. 101(1981)16
10. Y. Hiraoka, M. Okada and H. Irie, J. Nucl. Mat. 1555-157(1988) 381
11. Y. Hiraoka, Mater.Trans. JIM, 31(1990) 861
12. C. V. Robino, PhD dissertation, Lehigh Univ. 1988
13. N. Igata, A. Kohyama and K. Itadani, J. Nuc. Mat. 85-86(1979)895
14. A. Kohyama and N. Igata, J. Nuc. Mat. 122(1984)767
15. J. Wadsworth, G. R. Morse and P. M. Chewey, Mater. Sci. Eng. 59(1983)257
16. J. B. Brosse, R. Fillet and M. Biscondi, Scripta. Met. 15(1981)619
17. A. Kumar and B. L. Eyre, Proc. Roy. Soc. Lond. A370(1980)431
18. B. Tabering and N. Reheis, Intern. J. Refractory Metals and Hard Materials, 28(2010)728
19. F. Morito, J. Less-Common Met. 146(1989)337
20. F. Morito, J. Phys. IV, 1(1993)553
21. F. Morito, J. Mat. Sci. 24(1989)3403
22. F. Morito, J. Nuc. Mat.165(1989)142
23. F. Morito, Proc. 13th Intern. Plansee Seminar, Eds. H. Bildstein and R. EcK, 1(1993)585
24. F. Morito, JOM, 45(1993)54
25. F. Morito, Colloque de Physique, C1-51(1990)281
26. B. V. Zatolokin, Weld. Prod. 26(1979)7
27. Y. V. Milman, Auto. Weld. 33(1980)68
28. A. S. Wronski, A. C. Chilton and E. M. Capron, Acta Met. 17(1969)751
33
34. References-b
1. F. Morito, J. Mat. Sci, 24(1989)3403
2. F. Morito, J. Nuc. Mat. 165(1989)142
3. F. Morito, J. Less Common Met. 146(1989)337
4. F. Morito, Processing and Applications of High Purity Refractory Metals and Alloys, P.
Kumar, H. A. Jehn and M. Uz, eds. Pittsburgh, Pennsylvania, TMS, (1993), p.197-208
5. L. E. Davis, N. C. MacDonald, P. W. Palmberg, G. E. Riech and R. E. Weber, Handbook of
Auger Electron Spectroscopy, 2nd Ed. Physical Electronics Industries Inc. Eden Plairie,
Minnesota, 1976
6. F. Morito, Proc. 13th Intern. Plansee Seminar, H. Bildstein and R. EcK, eds. Reutte/Tirol,
1(1993)585
7. 栗下裕明, 久芳俊一, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)539
8. 栗下裕明, 大石朗, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)546
9. F. Morito, Proc. 12th Intern. Plansee Seminar, Eds. H. Bildstein and H. M. Ortner,
1(1989)313
10. F. Morito, Colloque de Physique, C1-51(1990)281
11. F. Morito, Vacuum, 41(1990)1743
12. F. Morito, JOM, 45(1993)54
13. Y. Hiraoka, F. Morito, M. Okada and R. Watanabe, J. Nuc. Mat. 78(1978)192
14. F. Morito, Proc. 12th International Plansee Seminar, H. Bildstein and H. M. Ortner, eds.
Reutte, Tirol, Austria, 1(1989)417
15. F. Morito, JOM, 45(1993)54
16. F. Morito, High Temperatures and High Pressures, 26(1994)101
17. F. Morito, J. Phys. IV, 1(1993)553
18. N. Igata, A. Kohyama and K. Itadani, J. Nuc. Mat. 85-86(1979)895
19. J. Wadsworth, C. M. Packer, P. M. Chewey and W. C. Coons, Mater. Sci. Eng.
59(1983)257
20. A. S. Wronski, A. C. Chilton and E. M. Capron, Acta Met. 17(1969)751
21. 栗下裕明, 久芳俊一, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)539
22. 栗下裕明, 大石朗, 久保晴義, 吉永日出男, 日本金属学会誌, 7(1983)546
23. A. V. Krajnikov, F. Morito and V. N. Slyunyaev, Intern. J. Refractory Metals and Hard
Materials, 15(1997)325
34
35. 24. H. Kurishita, H. Yoshinaga, K. Abi Ko, S. SuzuKi and H. Kimura, Trans. JIM,
27(1986)739)
25. H. Kurishita, O. To Kunaga and H. Yoshinaga, Mater. Trans. JIM, 31(1990)190
35
36. References-c
1. T.B. Massalski, Eds. Alloy Phase Diagrams, vol. 2, ASM International, Metals ParK, OH,
(1986)
2. G. A. Geach and J. R. Hughes, Proc. 2nd Plansee Seminar, Pergamon Press, London,
(1956)245
3. Von. I. Glass and G. Bohm, Planseeberichte. 10(1962)144
4. M. S. Duesbery, Dislocation in Solids, Elsevier Science Publishers, Netherlands, (1989)69
5. A. D. Korotaev, A. N. Tyumentsev and Yu. I. Pochivalovl, Proc. International Symposium
on Rhenium and Rhenium Alloys, B.D. Bryskin, ed. TMS, (1997)661
6. J. A. Shields Jr, Proc. 1992 Powder Metallurgy World Congress, Metal Powder Federation,
Princeton, NJ, 8(1992)199
7. J. A. Shields Jr, Adv. Mat. Proc. 1421(1992)28
8. R. L. Mannhreim and J. L. Garin, J. Materials Processing Techrnology, 143-144(2003)533
9. F. Morito, Proc.12th Plansee Seminar, Reutte, Tirol, Austria, 1(1989)417
10. F. Morito, Colloque de Physique, C1-51(1990)281
11. F. Morito, Surface and Interface Analysis, 15(1990)427
12. F. Morito, JOM, 45(1993)54
13. F. Morito, Proc. 13th Plansee Seminar, Reutte, Tirol, Austria, 1(1993)585
14. F. Morito, Proc. International Symposium on Rhenium and Rhenium Alloys, B.D.
Bryskin, ed. TMS, (1997)559
15. F. Morito, Proc. 14th Plansee Seminar, Reutte, Tirol, Austria, 1(1997)103
16. J. C. Carlen and B. D. Bryskin, J. Materials Engineering and Performance, 3(1994)282
17. I. Wesemann, A. Hoffmann, T. Mrotzek and U. Martin, Int. J. Ref. Met. Hard Mat.
28(2010)709
18. R. L. Fleischer, Acta Metall. 9 (1963) 203-209
19. H. Suzuki, Sci. Rep. Res. Inst. Tohoku Univ. A4 (1952) 455-463
20. R. A. Labusch, Phys. Status Solidi, B-41 (1970) 659-669
21. J. Xu, E. A. Kenik and T. Zhai, Phil. Mag. 88(2008)1543
22. J. Xu, E. A. Kenik and T. Zhai, Mater. Sci. Eng, A(2008)76
36
37. References-d
1. N. N. Morgunova, B. A. Klypin et al. Molybdenum Alloys, Moscow, Metallurgy, 1975
2. T. B. Massalski, Eds. Alloy Phase Diagrams, vol. 2, ASM International, Metals Park, OH,
1986
5. 3. R. A. Erck and L. E. Rehn, Phil. Mag. A62(1990)29
6. 4. A. Hasegawa, K. Ueda, M. Satou and K. Abe, J. Nuc. Mat. 258-263(1998)902
7. 5. Y. Nemoto, A. Hasegawa, M. Satou, K. Abe and Y. Hiraoka, J. Nuc. Mat. 324(2004)62
8. 6. Sh. Sh. Ibragimov, V. V. Kirsanov and Yu. S. Pjatiletov, Radiation Damage of Metals
and Alloys, Moscow, Energoatomizdat, (1995)210
9. 7. K. J. Leonard, J. T. Busby and S. J. Zinkle, J. Nuc. Mat. 366(2007)336
10. 8. K. J. Leonard, J. T. Busby and S. J. Zinkle, J. Nuc. Mat. 366(2007)369
11. 9. J. T. Busby, K. J. Leonard and S. J. Zinkle, J. Nuc. Mat. 366(2007)388
12. 10. E. J. Edwards, F. A. Garner and D. S. Gelles, J. Nuc. Mat. 375(2008)370
13. 11. F. Morito and K. Shiraishi, J. Nuc. Mat. 179-181(1991)592
14. 12. V. P. Chakin, F. Morito, V. A. Kaza Kov, Yu. D. Goncharenko and Z. E. Ostrovsky, J.
Nuc. Mat. 258-263(1998)883
15. 13. F. Morito, V. P. Chakin, Yu. D. Goncharenko, A. O. Posevin and L. A. Yevseev,
Microstructure evolution during high-temperature annealing in molybdenum-rhenium
alloys welds irradiated at low temperature, presented at ICFRM-11, Kyoto, Dec. 2003
16. 14. F. Morito, V. P. Chakin, H. Saito, N. I. Danylenko and A. V. Krajnikov, Proc. 17th
International Plansee Seminar, P. Rhoedhammer et al. Eds. Reutte/Tirol, vol. 1, (2009),
RM63
17. 15. F. Morito, V. P. Chakin, M. I. Danylenko and A. V. Krajnikov, J. Nuc. Mat. (2011),
doi;10.1016/j.jnucmat.2010.12.183
18. 16. F. Morito, Proc. 12th International Plansee Seminar, G. Kneringer et al. Eds.
Reutte/Tirol, 1(1989)417
19. 17. F. Morito, Proc. 13th International Plansee Seminar, G. Kneringer et al. Eds.
Reutte/Tirol, 1 (1993)585
20. 18. F. Morito, Proc. International Symposium on Rhenium and Rhenium Alloys, TMS,
(1997)559
21. 19. F. Morito, Proc. 14th International Plansee Seminar, G. Kneringer et al. Eds.
Reutte/Tirol, 1(1997)1037
37
38. 22. 20. V. A. Kazakov, A. S. Pokrovsky, A. V. Smirnov and L. I. Smirnova, Physics of
Metals and Metal Science, 42(1976)357
23. 21. V. A. Kazakov, A. S. Pokrovsky and A. V. Smirnov, Nuclear Technology,
53(1981)392
38
39. References <JNM-2010> 8
[1] S.R. Agnew and T. Leonhardt, JOM, 55(10), (2003) 25-29.
[2] R.W. Buckman, Jr., Proc. Nuclear Space Power Systems Materials Requirements, AIP,
699, (2004) 816-821.
[3] V.P. Chakin, Yu.A. Vlasov, V.A. Kazakov, Yu.D. Goncharenko and A.O. Posevin,
Prospective Materials, No.5, (2005) 50-56.
[4] M.S. El-Genk and J.-M. Tournier, Journal of Nuclear Materials, 340, (2005) 93-112.
[5] D.J. Olson, B. Mishra and D.W. Wenman, Mineral Processing and Extractive Metallurgy
Review, 22, (2001) 1-23.
[6] F. Morito and K. Shiraishi, Journal of Nuclear Materials, 179, (1991) 592-595.
[7] V.P. Chakin, F. Morito, V.A. Kazakov, Yu.D. Goncharenko and Z.E. Ostrovsky, Journal
of Nuclear Materials, 258-263 (1998) 883-888.
[8] F. Morito, V.P. Chakin, H. Saito, N.I. Danylenko and A.V. Krajnikov, Proc. 17th
International Plansee Seminar, P. Rhoedhammer et al. (Eds.), Reutte/Tirol, vol. 1, (2009)
RM63.
[9] F. Morito, Proc. 12th International Plansee Seminar, G. Kneringer et al. (Eds.),
Reutte/Tirol, vol. 1, (1989) 417-431.
[10] F. Morito, JOM, 45(6), (1993) 54-58.
[11] F. Morito, Proc. 13th International Plansee Seminar, G. Kneringer et al. (Eds.),
Reutte/Tirol, vol. 1, (1993) 585–598.
[12] A.V. Krajnikov, F. Morito and V.N. Slyunyaev, International Journal of Refractory
Metals and Hard Materials, 15, (1997) 305-339.
[13] F. Morito, T. Noda and A.V. Krajnikov, Proceedings International Conference on
Science for Materials in the Frontier of the Centuries: Advantages and Challenges, IPMS
NASU, Kiev, VI (2002) 140.
[14] H. Saito and F. Morito, Basics of Autoradiography and Its Application in Materials
Science and Engineering, H. Saito (Eds.), Urabe Publishing, Chiba, (2008) pp. 101-112.
[15] F. Morito, Journal de Physique, IV, 1, (1993) 553-556.
[16] F. Morito, Proc. 14th International Plansee Seminar, G. Kneringer et al. (Eds.),
Reutte/Tirol, vol. 1, (1997) 1037-1049.
[17] F. Morito, Proc. International Symposium on Rhenium and Rhenium Alloys, (1997) 559-
568.
[18] N.N. Morgunova, B.A. Klypin, et al., Molybdenum Alloys, Moscow, Metallurgy, 1975.
[19] T.B. Massalski, Eds., Alloy Phase Diagrams, vol. 2, ASM International, Metals Park,
OH, 1986.
[20] R.A. Erck and L.E. Rehn, Philosophical Magazine A, 62, (1990) 29-51.
[21] A. Hasegawa, K. Ueda, M. Satou and K. Abe, Journal of Nuclear Materials, 258-263,
(1998) 902-906.
[22] Y. Nemoto, A. Hasegawa, M. Satou and K. Abe, Journal of Nuclear Materials, 324,
39
40. (2004) 62-70.
[23] Sh.Sh. Ibragimov, V.V. Kirsanov and Yu.S. Pjatiletov, Radiation Damage of Metals and
Alloys, Moscow, Energoatomizdat, (1995) 210-213.
[24] K.J. Leonard, J.T. Busby and S.J. Zinkle, Journal of Nuclear Materials, 366, (2007) 369-
387
[25] E.J. Edwards, F.A. Garner and D.S. Gelles, Journal of Nuclear Materials, 375, (2008)
370-381.
40