Validating classical line profile analyses using microbeam diffraction from individual dislocation cell walls and cell interiors

2012 ◽  
Vol 45 (2) ◽  
pp. 157-165 ◽  
Author(s):  
Lyle E. Levine ◽  
Peter Geantil ◽  
Bennett C. Larson ◽  
Jonathan Z. Tischler ◽  
Michael E. Kassner ◽  
...  

Dislocation structures in deformed metals produce broad asymmetric diffraction line profiles. During analysis, these profiles are generally separated into two nearly symmetric subprofiles corresponding to diffraction by dislocation cell walls and cell interiors. These subprofiles are then interpreted using complex models of dislocation-based line broadening. Until now, it has not been possible to test the many assumptions that are made in such an analysis. Here, depth-resolved microbeam diffraction was used to measure diffraction line profiles from numerous individual dislocation cell walls and cell interiors in a heavily deformed Cu single crystal. Summing these profiles directly constructed the cell-interior and cell-wall subprofiles that have been approximated in the line profile analysis literature for the past 30 years. Direct comparison between the reconstructed subprofiles and the macroscopic asymmetric line profile from the same sample allows the first direct tests of many of the assumptions that have been used for interpreting these X-ray measurements.

2000 ◽  
Vol 33 (3) ◽  
pp. 964-974 ◽  
Author(s):  
J. I. Langford ◽  
D. Louër ◽  
P. Scardi

A distribution of crystallite size reduces the width of a powder diffraction line profile, relative to that for a single crystallite, and lengthens its tails. It is shown that estimates of size from the integral breadth or Fourier methods differ from the arithmetic mean of the distribution by an amount which depends on its dispersion. It is also shown that the form of `size' line profiles for a unimodal distribution is generally not Lorentzian. A powder pattern can be simulated for a given distribution of sizes, if it is assumed that on average the crystallites have a regular shape, and this can then be compared with experimental data to give refined parameters defining the distribution. Unlike `traditional' methods of line-profile analysis, this entirely physical approach can be applied to powder patterns with severe overlap of reflections, as is demonstrated by using data for nanocrystalline ceria. The procedure is compared with alternative powder-pattern fitting methods, by using pseudo-Voigt and Pearson VII functions to model individual line profiles, and with transmission electron microscopy (TEM) data.


2004 ◽  
Vol 27 (1) ◽  
pp. 59-67 ◽  
Author(s):  
K. Kapoor ◽  
D. Lahiri ◽  
S. V. R. Rao ◽  
T. Sanyal ◽  
B. P. Kashyap

2001 ◽  
Vol 378-381 ◽  
pp. 753-758
Author(s):  
Alexandre Boulle ◽  
C. Legrand ◽  
P. Thomas ◽  
R. Guinebretière ◽  
J.P. Mercurio ◽  
...  

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