Hostname: page-component-8448b6f56d-dnltx Total loading time: 0 Render date: 2024-04-23T19:06:53.025Z Has data issue: false hasContentIssue false
  • English
  • Français

Evolution of texture and dislocation distributions in high-ductile austenitic steel during deformation

Published online by Cambridge University Press:  05 March 2012

Shigeo Sato ,
Toshiki Yoshimura ,
Yohei Takahashi ,
Nao Yamada ,
Kazuaki Wagatsuma  and
Shigeru Suzuki
Shigeo Sato*
Affiliation:
Institute for Materials Research, Tohoku University, Sendai 980-8577, Japan
Toshiki Yoshimura
Affiliation:
Institute of Multidisciplinary Research for Advanced Materials, Tohoku University, Sendai 980-8577, Japan
Yohei Takahashi
Affiliation:
Department of Research, Nissan Arc, Ltd., Yokosuka 237-0061, Japan
Nao Yamada
Affiliation:
Anton Paar Japan K.K., Shinagawa-Ku, Tokyo 140-0001, Japan
Kazuaki Wagatsuma
Affiliation:
Institute for Materials Research, Tohoku University, Sendai 980-8577, Japan
Shigeru Suzuki
Affiliation:
Institute of Multidisciplinary Research for Advanced Materials, Tohoku University, Sendai 980-8577, Japan
*
a)Author to whom correspondence should be addressed. Electronic mail: s.sato@imr.tohoku.ac.jp
Get access Rights & Permissions [Opens in a new window]

Abstract

The microstructural evolution of Fe–Mn–C austenitic steels, which exhibit outstanding high-ductile deformation in their plastic regions, was characterized by line-profile and texture analyses. The convolutional multiple whole profile fitting procedure was used for a line-profile analysis of 2θ−θ diffraction data to evaluate variations of crystallite size, dislocation density, and dislocation arrangement. A substantial refinement of the crystallite size proceeded at an early deformation stage. In addition, the dislocation density increased with an increase in the tensile strain. Texture evolution was characterized by the analysis of orientation distribution functions. Three texture components grew with an increase in the tensile strain. According to the pole figure describing the full width at half maximum (FWHM) distribution of the 220 reflection, the nontextured grains had more microstructural defects than the textured grains. To evaluate the microstructural defects in detail, the 220 reflection observed at each texture orientation was analyzed by the single-line-profile method. The crystallite size and dislocation density were almost comparable, irrespective of the kind of texture component. The crystallite size of the nontextured grains was also comparable to that of the textured grains, whereas the nontextured grains had a dislocation density several times that of the textured grains.

Keywords

line-profile analysistexture analysisdislocationcrystallitetwo-dimensional detector
Type
Technical Articles
Information
Powder Diffraction , Volume 26 , Special Issue 2 , June 2011 , pp. 129 - 133
Copyright
Copyright © Cambridge University Press 2011

Access options

Get access to the full version of this content by using one of the access options below. (Log in options will check for institutional or personal access. Content may require purchase if you do not have access.)

References

Barbier, D., Gey, N., Allain, S., Bozzolo, N., and Humbert, M. (2009). “Analysis of the tensile behavior of a TWIP steel based on the texture and microstructure evolutions,” Mater. Sci. Eng., A MSAPE3 500, 196–206. 10.1016/j.msea.2008.09.031CrossRefGoogle Scholar
de Keijser, Th. H., Langford, J. I., Mittemeijer, E. J., and Vogels, A. B. P. (1982). “Use of the Voigt function in a single-line method for the analysis of X-ray diffraction line broadening,” J. Appl. Crystallogr. JACGAR 15, 308–314. 10.1107/S0021889882012035CrossRefGoogle Scholar
Gutierrez-Urrutia, I., Zaefferer, S., and Raabe, D. (2010). “The effect of grain size and grain orientation on deformation twinning in a Fe–22 wt.% Mn–0.6 wt.% C TWIP steel,” Mater. Sci. Eng., A MSAPE3 527, 3552–3560. 10.1016/j.msea.2010.02.041CrossRefGoogle Scholar
Harjo, S., Tomota, Y., Lukáš, P., Neov, D., Vrána, M., Mikula, P., and Ono, M. (2001). “In situ neutron diffraction study of α−γ Fe–Cr–Ni alloys under tensile deformation,” Acta Mater. ACMAFD 49, 2471–2479. 10.1016/S1359-6454(01)00147-1CrossRefGoogle Scholar
Hielscher, R., and Schaeben, H. (2008). “A novel pole figure inversion method: Specification of the MTEX algorithm,” J. Appl. Crystallogr. JACGAR 41, 1024–1037. 10.1107/S0021889808030112CrossRefGoogle Scholar
Ribarik, G., Gubicza, J., and Ungar, T. (2004). “Correlation between strength and microstructure of ball-milled Al–Mg alloys determined by X-ray diffraction,” Mater. Sci. Eng., A MSAPE3 387–389, 343–347. 10.1016/j.msea.2004.01.089CrossRefGoogle Scholar
Suzuki, S., Senoo, S., Maruyama, T., and Shinoda, K. (2008). “Characteristic structural changes in stress-induced martensitic transformation and reverse transformation of a polycrystalline Fe–Mn–Si Alloy,” Mater. Trans. MTARCE 49, 2755–2760. 10.2320/matertrans.MRA2008211CrossRefGoogle Scholar
Ungár, T., and Borbely, A. (1996). “The effect of dislocation contrast on x-ray line broadening: A new approach to line profile analysis,” Appl. Phys. Lett. APPLAB 69, 3173–3175. 10.1063/1.117951CrossRefGoogle Scholar
Williamson, G. K., and Smallman, R. E. (1956). “Dislocation densities in some annealed and cold-worked metals from measurements on the X-ray Debye-Scherrer spectrum,” Philos. Mag. PMHABF 1, 34–36. 10.1080/14786435608238074CrossRefGoogle Scholar