“…The kind of representation has become known and used as the Williamson–Hall plot (Williamson and Hall, 1953). The numbering in the figure means (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2) Cu filings (Brindley, 1940), (3) Cu filings (Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Figure 1.(a) Williamson-Hall plots of (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2, 3) Cu filings (Brindley, 1940; Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937); (b) Wagner plot of ball-milled tungsten-carbide (Aqua and Wagner, 1966; Gillies and Lewis, 1968). Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937).…”
Section: The Beginning Of X-ray Line Profile Analysismentioning
confidence: 99%
“…(a) Williamson-Hall plots of (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2, 3) Cu filings (Brindley, 1940; Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937); (b) Wagner plot of ball-milled tungsten-carbide (Aqua and Wagner, 1966; Gillies and Lewis, 1968). …”
Section: The Beginning Of X-ray Line Profile Analysismentioning
Dislocation model of strain anisotropy is presented. The dislocation theorem of strain broadening is suggested which means that strain broadening can only be caused by dislocation-type lattice defects. Based on this theorem strain anisotropy is modeled and accounted for by assuming that strain broadening is caused by dislocations or dislocation-type lattice defects. The effect of strain anisotropy is summarized in hkl dependent dislocation contrast factors, which can be either averaged over the permutations of hkl indices or are different for each different reflection. The dislocation model of strain anisotropy provides a powerful tool to analyze slip activity, Burgers vector populations, and plasticity on the basis of line profile analysis.
“…The kind of representation has become known and used as the Williamson–Hall plot (Williamson and Hall, 1953). The numbering in the figure means (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2) Cu filings (Brindley, 1940), (3) Cu filings (Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Figure 1.(a) Williamson-Hall plots of (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2, 3) Cu filings (Brindley, 1940; Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937); (b) Wagner plot of ball-milled tungsten-carbide (Aqua and Wagner, 1966; Gillies and Lewis, 1968). Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937).…”
Section: The Beginning Of X-ray Line Profile Analysismentioning
confidence: 99%
“…(a) Williamson-Hall plots of (1) aluminum filings (unpublished data by G. K. Williamson and W. H. Hall), (2, 3) Cu filings (Brindley, 1940; Stokes et al , 1943), (4, 5, 6) Cu sheet reduced to 20%, 60%, 99.5%, respectively (Dehlinger and Kochendoerfer, 1939; Dehlinger and Schäcke, 1943), (7, 8) Rhodium filings (Jaswon and Wheeler, 1948), and (9) Martensite rod (Jones and Sykes, 1937); (b) Wagner plot of ball-milled tungsten-carbide (Aqua and Wagner, 1966; Gillies and Lewis, 1968). …”
Section: The Beginning Of X-ray Line Profile Analysismentioning
Dislocation model of strain anisotropy is presented. The dislocation theorem of strain broadening is suggested which means that strain broadening can only be caused by dislocation-type lattice defects. Based on this theorem strain anisotropy is modeled and accounted for by assuming that strain broadening is caused by dislocations or dislocation-type lattice defects. The effect of strain anisotropy is summarized in hkl dependent dislocation contrast factors, which can be either averaged over the permutations of hkl indices or are different for each different reflection. The dislocation model of strain anisotropy provides a powerful tool to analyze slip activity, Burgers vector populations, and plasticity on the basis of line profile analysis.
In beiden Fallen werden keine nachweisbaren Tnbensitatsiinderungen festgestellt.Die bisherigen Untersuchungen mit davon verschiedenen Ergebnissen werden diskutiert.
1. Es wurde ein unter überspanntem Wasserdampf hergestellter mikrokristalliner Böhmit übermikroskopisch auf Kristallgröße und ‐form und röntgenographisch auf mittlere Primärteilchendimensionen hin untersucht. Letztere lagen wesentlich unter den Kristallabmessungen.
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