Pub Date : 1984-06-01DOI: 10.1179/030634584790419999
S. Messoloras, B. Pike, R. Stewart, C. Windsor
AbstractSmall angle neutron scattering was used to study the precipitation in two iron–chromium–aluminium alloys of similar composition, the main difference being the addition of yttrium to one alloy. The mean diameter, separation, and volume fraction of the precipitates is determined as a function of aging time and temperature. The two alloys behaved differently, the precipitate growing more quickly in the yttrium containing alloy. The upper limit of stability of the chromium rich phase was established as lying between 480 and 485°C in both alloys.
{"title":"Precipitation in iron–chromium–aluminium alloys","authors":"S. Messoloras, B. Pike, R. Stewart, C. Windsor","doi":"10.1179/030634584790419999","DOIUrl":"https://doi.org/10.1179/030634584790419999","url":null,"abstract":"AbstractSmall angle neutron scattering was used to study the precipitation in two iron–chromium–aluminium alloys of similar composition, the main difference being the addition of yttrium to one alloy. The mean diameter, separation, and volume fraction of the precipitates is determined as a function of aging time and temperature. The two alloys behaved differently, the precipitate growing more quickly in the yttrium containing alloy. The upper limit of stability of the chromium rich phase was established as lying between 480 and 485°C in both alloys.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"17 5 1","pages":"311-321"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"75123648","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790420023
K. Suganuma, H. Kayano
AbstractThe characteristics of the irradiation embrittlement of some ferritic stainless steels were examined by tensile tests. Steels selected in this investigation were classified into three groups: X phase, precipitation hardened Fe-13Cr steels; tempered martensitic Fe-12Cr steels; and low alloy steels. The latter steels were chosen in order to compare the irradiation embrittlement characteristics with those of stainless steels. The stainless steels were superior to the low alloy steels with regard to the irradiation embrittlement (the changes in both ductile–brittle transition temperature (DBTT) and unstable plastic flow transition temperature (UPFTT)), irrespective of whether these stainless steels had X phase precipitated structures or tempered martensitic structures. The suppression of the DBTT increase owing to irradiation results from low yield stress increase ∆σy and high |[dσy(u)/dT]|, where u denotes unirradiated, in the stainless steels. The suppression of the UPFTT results from the high work ...
{"title":"Irradiation embrittlement of ferritic stainless steels","authors":"K. Suganuma, H. Kayano","doi":"10.1179/030634584790420023","DOIUrl":"https://doi.org/10.1179/030634584790420023","url":null,"abstract":"AbstractThe characteristics of the irradiation embrittlement of some ferritic stainless steels were examined by tensile tests. Steels selected in this investigation were classified into three groups: X phase, precipitation hardened Fe-13Cr steels; tempered martensitic Fe-12Cr steels; and low alloy steels. The latter steels were chosen in order to compare the irradiation embrittlement characteristics with those of stainless steels. The stainless steels were superior to the low alloy steels with regard to the irradiation embrittlement (the changes in both ductile–brittle transition temperature (DBTT) and unstable plastic flow transition temperature (UPFTT)), irrespective of whether these stainless steels had X phase precipitated structures or tempered martensitic structures. The suppression of the DBTT increase owing to irradiation results from low yield stress increase ∆σy and high |[dσy(u)/dT]|, where u denotes unirradiated, in the stainless steels. The suppression of the UPFTT results from the high work ...","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"30 1","pages":"281-285"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"84713621","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790420050
J. Kennedy
AbstractAcoustic emission detected during tensile deformation of commercial grade 7075 aluminium was analysed to determine the influence of the aged (T6) and overaged (T73) tempers on emission behaviour. A comparison of acoustic emission accumulation rates as a function of strain for both tempers showed that the T6 temper had a higher rate over the strain range of 1–4%. Beyond 4% strain, the acoustic emission rates for each temper were about equal and gradually decreased up to necking. It was concluded that two separate sources were responsible for emission in the T6 temper, including dislocation shearing of GP zones and the fracture of coarse intermetallic particles. In the T73 temper, emission was attributed mainly to the fracture of coarse intermetallic particles.
{"title":"Acoustic emission during deformation of heat treated 7075 aluminium","authors":"J. Kennedy","doi":"10.1179/030634584790420050","DOIUrl":"https://doi.org/10.1179/030634584790420050","url":null,"abstract":"AbstractAcoustic emission detected during tensile deformation of commercial grade 7075 aluminium was analysed to determine the influence of the aged (T6) and overaged (T73) tempers on emission behaviour. A comparison of acoustic emission accumulation rates as a function of strain for both tempers showed that the T6 temper had a higher rate over the strain range of 1–4%. Beyond 4% strain, the acoustic emission rates for each temper were about equal and gradually decreased up to necking. It was concluded that two separate sources were responsible for emission in the T6 temper, including dislocation shearing of GP zones and the fracture of coarse intermetallic particles. In the T73 temper, emission was attributed mainly to the fracture of coarse intermetallic particles.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"1 1","pages":"286-288"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"84082009","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790420005
H. Kabassis, J. Rutter, W. Winegard
Abstract This communication presents confirmation of the recent work by Evans and Prince on the Bi-In phase diagram (Fig. 1), especially that portion lying between the compounds BiIn and BiIn2 The structure of the Bi3Ins-BiIn2 eutectic is also reported.
{"title":"Bi-In system: phase diagram and some eutectic structures","authors":"H. Kabassis, J. Rutter, W. Winegard","doi":"10.1179/030634584790420005","DOIUrl":"https://doi.org/10.1179/030634584790420005","url":null,"abstract":"Abstract This communication presents confirmation of the recent work by Evans and Prince on the Bi-In phase diagram (Fig. 1), especially that portion lying between the compounds BiIn and BiIn2 The structure of the Bi3Ins-BiIn2 eutectic is also reported.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"2 1","pages":"326-328"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"82025446","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790420069
S. Kerry, V. Scott
AbstractPrecipitates which form on {111} planes of the Al-Cu-Mg alloy lattice when small amounts of silver are added are newly established as having a hexagonal structure with a = 0.496 nm and c/a = 1.414. The [0001] direction in the precipitate is aligned parallel to a 〈111〉 direction in aluminium with 〈1010〉 parallel to 〈110〉, giving close registry of the respective crystal lattices. A small addition of zinc reduces the size of precipitate but does not change the crystal structure.
{"title":"Structure and orientation relationship of precipitates formed in Al-Cu-Mg-Ag alloys","authors":"S. Kerry, V. Scott","doi":"10.1179/030634584790420069","DOIUrl":"https://doi.org/10.1179/030634584790420069","url":null,"abstract":"AbstractPrecipitates which form on {111} planes of the Al-Cu-Mg alloy lattice when small amounts of silver are added are newly established as having a hexagonal structure with a = 0.496 nm and c/a = 1.414. The [0001] direction in the precipitate is aligned parallel to a 〈111〉 direction in aluminium with 〈1010〉 parallel to 〈110〉, giving close registry of the respective crystal lattices. A small addition of zinc reduces the size of precipitate but does not change the crystal structure.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"18 1","pages":"289-294"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"79145775","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790420014
H. Kabassis, J. Rutter, W. Winegard
Abstract Two ternary eutectic reactions are known to occur in the Bi-Cd-In ternary system: one takes place at 334.6 K and the other at 350,6 K. Experiments were conducted to determine the microstructures that result from these eutectic reactions, as well as the phases present and the volume fraction of each phase. The phases present in the 334.6 K eutectic are the major phase (BiIn2), Cd solid solution, and an In rich phase which subsequently decomposes eutectoidally. The room temperature In phase is α In. Lamellae of both minor phases are embedded in the major phase with a configuration ABCBA…, similar to that of the Cd-Pb-Sn ternary eutectic. A represents the BiIn2 phase, B the In rich phase, and C the Cd rich phase. The measured volume fractions are 60%BiIn2 4%Cd, and 36% In rich phase. The phases present in the 350.6 K eutectic are BiIn2, BiIn, and Cd solid solution. The structure, which is not regular, consists of the major phase (BiIn2) in which are embedded perforated plates of the BiIn phase and t...
{"title":"Microstructure of ternary eutectic alloys in Bi-Cd-In system","authors":"H. Kabassis, J. Rutter, W. Winegard","doi":"10.1179/030634584790420014","DOIUrl":"https://doi.org/10.1179/030634584790420014","url":null,"abstract":"Abstract Two ternary eutectic reactions are known to occur in the Bi-Cd-In ternary system: one takes place at 334.6 K and the other at 350,6 K. Experiments were conducted to determine the microstructures that result from these eutectic reactions, as well as the phases present and the volume fraction of each phase. The phases present in the 334.6 K eutectic are the major phase (BiIn2), Cd solid solution, and an In rich phase which subsequently decomposes eutectoidally. The room temperature In phase is α In. Lamellae of both minor phases are embedded in the major phase with a configuration ABCBA…, similar to that of the Cd-Pb-Sn ternary eutectic. A represents the BiIn2 phase, B the In rich phase, and C the Cd rich phase. The measured volume fractions are 60%BiIn2 4%Cd, and 36% In rich phase. The phases present in the 350.6 K eutectic are BiIn2, BiIn, and Cd solid solution. The structure, which is not regular, consists of the major phase (BiIn2) in which are embedded perforated plates of the BiIn phase and t...","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"11 1","pages":"322-325"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"77742646","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790419971
G. Humpston, B. L. Davies
AbstractAuSn is a compound that melts congruently and which has been shown by previous work to come into quasibinary eutectic equilibrium with Pb. Because there is some disagreement in the results of previous workers, a redetermination of the AuSn-Pb section has been undertaken before the investigation of the total constitution of the Au-Pb-Sn ternary system.
{"title":"Thermal analysis of AuSn-Pb quasibinary section","authors":"G. Humpston, B. L. Davies","doi":"10.1179/030634584790419971","DOIUrl":"https://doi.org/10.1179/030634584790419971","url":null,"abstract":"AbstractAuSn is a compound that melts congruently and which has been shown by previous work to come into quasibinary eutectic equilibrium with Pb. Because there is some disagreement in the results of previous workers, a redetermination of the AuSn-Pb section has been undertaken before the investigation of the total constitution of the Au-Pb-Sn ternary system.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"27 1","pages":"329-331"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"91544023","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-06-01DOI: 10.1179/030634584790419980
G. C. Allen
AbstractThe surface composition of some Magnox alloys etched in citric acid has been examined by secondary ion mass spectrometry and ion scattering spectroscopy. An enrichment of carbon containing species in the outermost regions of the surface was indicated, with an oxide–hydroxide layer containing enhanced quantities of aluminium, the main alloying element of the bulk metal, and the trace impurities iron, zinc, calcium (potassium), copper, manganese, silicon, and beryllium. The latter is difficult to detect by other methods but its identification using these techniques indicates that, as aluminium, it may be considered to playa role in the formation of the initial oxide layer.
{"title":"Surface analysis of etched Magnox alloys by secondary ion mass spectrometry and ion scattering spectroscopy","authors":"G. C. Allen","doi":"10.1179/030634584790419980","DOIUrl":"https://doi.org/10.1179/030634584790419980","url":null,"abstract":"AbstractThe surface composition of some Magnox alloys etched in citric acid has been examined by secondary ion mass spectrometry and ion scattering spectroscopy. An enrichment of carbon containing species in the outermost regions of the surface was indicated, with an oxide–hydroxide layer containing enhanced quantities of aluminium, the main alloying element of the bulk metal, and the trace impurities iron, zinc, calcium (potassium), copper, manganese, silicon, and beryllium. The latter is difficult to detect by other methods but its identification using these techniques indicates that, as aluminium, it may be considered to playa role in the formation of the initial oxide layer.","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"92 1","pages":"295-298"},"PeriodicalIF":0.0,"publicationDate":"1984-06-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"81608827","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-05-01DOI: 10.1179/030634584790420131
P. Bowen, J. Knott
AbstractMeasurements of microscopic cleavage fracture stress σF* and fracture toughness K 1C at low temperatures have been made on A 533 B, in an autotempered martensitic condition, to assess the effect of austenitizing temperature on fracture in a system where the fracture mode is transgranular quasicleavage for all austenitizing temperatures. A wide range of prior austenite grain sizes (and hence packet sizes) has been studied, and detailed microstructural information has been obtained in an attempt to gain a clear understanding of the mechanisms of cleavage fracture in this steel. The microscopic cleavage fracture stress is found to be independent of austenitizing temperature, and in the temperature range from −100 to −160°C it is also independent of temperature. At −196°C, the value of σF* falls slightly. The temperature independence of σF* strongly suggests a tensile stress controlled fracture criterion. The coarse grained condition exhibits higher strength, slightly higher fracture toughness, and a ...
{"title":"Cleavage fracture of A 533 B pressure vessel steel in martensitic condition","authors":"P. Bowen, J. Knott","doi":"10.1179/030634584790420131","DOIUrl":"https://doi.org/10.1179/030634584790420131","url":null,"abstract":"AbstractMeasurements of microscopic cleavage fracture stress σF* and fracture toughness K 1C at low temperatures have been made on A 533 B, in an autotempered martensitic condition, to assess the effect of austenitizing temperature on fracture in a system where the fracture mode is transgranular quasicleavage for all austenitizing temperatures. A wide range of prior austenite grain sizes (and hence packet sizes) has been studied, and detailed microstructural information has been obtained in an attempt to gain a clear understanding of the mechanisms of cleavage fracture in this steel. The microscopic cleavage fracture stress is found to be independent of austenitizing temperature, and in the temperature range from −100 to −160°C it is also independent of temperature. At −196°C, the value of σF* falls slightly. The temperature independence of σF* strongly suggests a tensile stress controlled fracture criterion. The coarse grained condition exhibits higher strength, slightly higher fracture toughness, and a ...","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"23 1","pages":"225-235"},"PeriodicalIF":0.0,"publicationDate":"1984-05-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"89748766","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1984-05-01DOI: 10.1179/030634584790420113
D. Mclean
AbstractIndividual experiments on the growth at elevated temperature of γ′ particles in nickel alloys do not cover a range of conditions sufficient to permit unambiguous discrimination between the growth laws a = (kt)⅓ and a = (k′t)½, where a is half the mean particle size (half the cube edge or sphere diameter as appropriate), k and k′ are constants, and t is time. This paper assembles six studies of Ni-Al binary alloys, Ni-Cr-Al ternary alloys, and the commercial IN 738 alloy, which together cover temperatures from 500 to 1000°C. By compensating for temperature and composition according to the theory from which the growth laws are derived, the experimental times are converted to equivalent times, which range from a few minutes to 50 years. The plot of a = (kt)⅓ over this considerable time span is linear, but that of a = (k′t)½ has the curved form to be expected when the former is linear. Growth of γ′ particles in these alloys, therefore, is correctly described, within the experimental times, by the firs...
{"title":"Predicting growth of γ′ in nickel alloys","authors":"D. Mclean","doi":"10.1179/030634584790420113","DOIUrl":"https://doi.org/10.1179/030634584790420113","url":null,"abstract":"AbstractIndividual experiments on the growth at elevated temperature of γ′ particles in nickel alloys do not cover a range of conditions sufficient to permit unambiguous discrimination between the growth laws a = (kt)⅓ and a = (k′t)½, where a is half the mean particle size (half the cube edge or sphere diameter as appropriate), k and k′ are constants, and t is time. This paper assembles six studies of Ni-Al binary alloys, Ni-Cr-Al ternary alloys, and the commercial IN 738 alloy, which together cover temperatures from 500 to 1000°C. By compensating for temperature and composition according to the theory from which the growth laws are derived, the experimental times are converted to equivalent times, which range from a few minutes to 50 years. The plot of a = (kt)⅓ over this considerable time span is linear, but that of a = (k′t)½ has the curved form to be expected when the former is linear. Growth of γ′ particles in these alloys, therefore, is correctly described, within the experimental times, by the firs...","PeriodicalId":18750,"journal":{"name":"Metal science","volume":"23 1","pages":"249-256"},"PeriodicalIF":0.0,"publicationDate":"1984-05-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"84969661","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
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