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A TEM study of the crystallography of lath-shaped austenite precipitates in a duplex stainless steel

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Abstract

The morphology of austenite (fcc) precipitates in a duplex stainless steel (DSS) is dominated by rods distributed in a ferrite (bcc) matrix. Minority of austenite precipitates also exhibits a lath shape, a common morphology in fcc to bcc transformations rather than a bcc to fcc transformation in a DSS. While the rod-shaped austenite precipitates in a DSS have been interpreted in previous investigations, precipitates with a lath shape were not well understood. This study focused on the lath-shaped austenite by using transmission electron microscopy. The habit plane of lath-shaped austenite was observed to be free of dislocations, but one array of dislocations was observed in the major side facet with a spacing of 9.6 nm and Burgers vector of [110]f/2|[010]b. These observations of crystallographic features were interpreted consistently by an O-line and good matching site analysis. Different morphologies in a DSS and similar morphologies in fcc to bcc and bcc to fcc transformations are compared and discussed.

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Notes

  1. The morphology of precipitates in fcc/bcc systems was mainly distinguished by the cross-sectional shape. The aspect ratio (width to thickness) of lath shape is around 2–4, while the aspect ratio for rod shape is around 1.

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Acknowledgements

Supports from National Natural Science Foundation of China (No. 51471097 and No. 51671111) and helpful discussions from Dr. Dong Qiu are gratefully acknowledged.

Author information

Authors and Affiliations

  1. Key Laboratory of Advanced Materials (MOE), School of Materials Science and Engineering, Tsinghua University, Beijing, 100084, People’s Republic of China

    Juan Du & Wen-Zheng Zhang

  2. CEMES-CNRS and Université de Toulouse, 29 rue J. Marvig, 31055, Toulouse, France

    Frédéric Mompiou

Authors
  1. Juan Du
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  2. Frédéric Mompiou
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  3. Wen-Zheng Zhang
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Corresponding author

Correspondence to Wen-Zheng Zhang.

Appendix

Appendix

The experimentally measured orientation matrix b M f was determined by the two pairs of parallel direction in Eq. 1 as

$$ {}_{\text{b} }\textbf{M}_{\text{f} } = \left[ {\begin{array}{*{20}c} {0.67} & { - 0.74} & {0.07} \\ {0.74} & {0.65} & { - 0.17} \\ {0.08} & {0.17} & {0.98} \\ \end{array} } \right] $$
(10)

In the O-line condition with the minimum interfacial energy of O-line interfaces, the transformation matrix A and displacement matrix T were determined as

$$ \textbf{A} = \left[ {\begin{array}{*{20}c} {1.12} & {0.07} & {0.06} \\ { - 0.08} & {1.11} & {0.14} \\ { - 0.07} & { - 0.20} & {0.78} \\ \end{array} } \right] $$
(11a)

and

$$ \textbf{T} = \textbf{I} - \textbf{A}^{ - 1} = \left[ {\begin{array}{*{20}c} {0.12} & {0.07} & {0.06} \\ { - 0.05} & {0.13} & {0.16} \\ { - 0.10} & { - 0.21} & { - 0.23} \\ \end{array} } \right] , $$
(11b)

where I is a unit matrix. The orientation matrix M is related to A by

$$ \textbf{M} = \textbf{CA}^{ - 1} /(\textbf{a}_{\rm f} /\textbf{a}_{\rm b} ) = \left[ {\begin{array}{*{20}c} {0.66} & { - 0.75} & {0.08} \\ {0.75} & {0.64} & { - 0.17} \\ {0.08} & {0.17} & {0.98} \\ \end{array} } \right] , $$
(12)

where C is the Bain correspondence matrix. The column vectors of C are given by [110], \( [\overline{1}10] \) and [001] corresponding to the OR in Eq. 3.

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Du, J., Mompiou, F. & Zhang, WZ. A TEM study of the crystallography of lath-shaped austenite precipitates in a duplex stainless steel. J Mater Sci 52, 11688–11700 (2017). https://doi.org/10.1007/s10853-017-1324-y

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