EBSD investigation of the crystallographic features of deformation-induced martensite in stainless steel

doi:10.1016/j.jmst.2020.08.023

Abstract

Abstract:

Variant selection during the martensitic transformation in steels may play an important role in determining the transformation kinetics and the resulting mechanical properties. In this study, the variant selection and crystallographic features of deformation-induced martensite were investigated by quasi in situ electron backscatter diffraction (EBSD) in grade SUS321 during tensile deformation. Significant differences in variant selection between austenite (γ)→hcp-martensite (ε)→bcc-martensite (α’) and γ→α’ transformation routes were observed and reported in detail, which demonstrated that ε-martensite plays an important role in the variant selection of α’. Variant selection at different deformation stages was also analysed and revealed that α’ variants with the highest priority and variant pairs were preferred at the initial and last deformation stages in the γ→ε→α’ sequence, respectively. Meanwhile, the single α’ variant nucleated at the thin slip band keeps its crystallography feature upon further deformation in the γ→α’ sequence. In addition, the strain work of the martensitic transformation for applied loads was quantitatively estimated to explain the variant selection and associated mechanism. When these calculations are compared to the experimental results it is found that they are not able to predict which α’ variant is forming preferentially during either during the γ→α’ or the ε→α’ sequences, while only accurate predictions are obtained for the γ→ε transformation which indicates that the γ→α’ variant selection is more complex.

Key words: Deformation-induced martensitic transformation, Austenitic steels, Variant selection, Crystallographic orientation

Jinliang Wang, Minghao Huang, Jun Hu, Chenchong Wang, Wei Xu. EBSD investigation of the crystallographic features of deformation-induced martensite in stainless steel[J]. J. Mater. Sci. Technol., 2021, 69: 148-155.

Figures/Tables 7

Table 1 Chemical composition (wt. %) and SFE (mJ/m2) of the investigated alloy[30].

Type	Fe	Cr	Ni	C	Si	Mn	Ti	SFE
SUS321	Bal.	17.6	9.22	0.015	0.52	1.23	0.088	20

Fig. 1. (a) Schematic illustrations of a micro-tensile specimen where the points of monitoring for the strain (black symbols) and the EBSD scan (red symbol) are marked. (b) The locations of area A and B and the inverse pole figure (IPF) maps for γ in two areas before deformation.

Fig. 2. The crystallographic characteristics of ε and α’ in area A (grain 1, Fig. 1) during deformation. (a-c) ε (magenta area) and α’ (the rest colour area) IPF maps obtained by EBSD for the directions parallel to the rolling direction of the sample (the upper right corners in Fig. 2(a) and (b) also show the IPF maps for the directions parallel to the tangential direction of the sample; the upper right corner in Fig. 2(c) shows the phase map with special grain boundaries, where blue and white lines represent the 60 ° and 50.48 ° grain boundary, respectively). (d-f) Pole figures for γ, ε and α’, respectively. Note: (a-c) were obtained by HKL channel 5 software; (d-f) were obtained by using the MATLAB-based toolbox MTEX.

Table 2 The 4 potential ε variants in the S-N relationship.

Variant No.		Parallel plane	Parallel direction	Slip plane and direction
ε1	ε1-1	(111) γ //(0002) ε	[10-1] γ//[2-1-10] ε	(111)[11-2]
	ε1-2		[-110] γ//[2-1-10] ε	(111)[-211]
	ε1-3		[0-11] γ//[2-1-10] ε	(111)[1-21]
ε2	ε2-1	(1-11) γ //(0002) ε	[0-1-1] γ//[2-1-10] ε	(1-11)[1-1-2]
	ε2-2		[110] γ//[2-1-10] ε	(1-11)[-2-11]
	ε2-3		[-101] γ//[2-1-10] ε	(1-11)[121]
ε3	ε3-1	(-111) γ //(0002) ε	[01-1] γ//[2-1-10] ε	(-111)[-11-2]
	ε3-2		[-1-10] γ//[2-1-10] ε	(-111)[211]
	ε3-3		[101] γ//[2-1-10] ε	(-111)[-1-21]
ε4	ε4-1	(11-1) γ //(0002) ε	[-10-1] γ//[2-1-10] ε	(11-1)[112]
	ε4-2		[1-10] γ//[2-1-10] ε	(11-1)[-21-1]
	ε4-3		[011] γ//[2-1-10] ε	(11-1)[1-2-1]

Table 3 The 24 potential α’ variants in the K-S relationship[33].

Variant No.	Parallel plane	Parallel direction	Variant No.	Parallel plane	Parallel direction
V1	(111) γ //(011) α’	[-101] γ//[-1-11] α’	V13	(-111) γ //(011) α’	[0-11] γ//[-1-11] α’
V2		[-101] γ//[-11-1] α’	V14		[0-11] γ//[-11-1] α’
V3		[01-1] γ//[-1-11] α’	V15		[-10-1] γ//[-1-11] α’
V4		[01-1] γ//[-11-1] α’	V16		[-10-1] γ//[-11-1] α’
V5		[1-10] γ//[-1-11] α’	V17		[110] γ//[-1-11] α’
V6		[1-10] γ//[-11-1] α’	V18		[110] γ//[-11-1] α’
V7	(1-11) γ //(011) α’	[10-1] γ//[-1-11] α’	V19	(11-1) γ //(011) α’	[-110] γ//[-1-11] α’
V8		[10-1] γ//[-11-1] α’	V20		[-110] γ//[-11-1] α’
V9		[-1-10] γ//[-1-11] α’	V21		[0-1-1] γ//[-1-11] α’
V10		[-1-10] γ//[-11-1] α’	V22		[0-1-1] γ//[-11-1] α’
V11		[011] γ//[-1-11] α’	V23		[101] γ//[-1-11] α’
V12		[011] γ//[-11-1] α’	V24		[101] γ//[-11-1] α’

Fig. 3. The crystallographic characteristics of α’ in area B (Fig. 1) during deformation. (a-c) α’ IPF maps obtained by EBSD for the directions parallel to the rolling direction of the sample (the lower right corner in Fig. 3a also shows the α’ IPF map for the directions parallel to the tangential direction of the sample). (d-e) Pole figures of γ and α’, respectively. Note: (a-c) were obtained by HKL channel 5 software; (d-e) were obtained by using the MATLAB-based toolbox MTEX.

Fig. 4. The calculated value of strain works for ε and α’ transformation under 200 MPa uniaxial tensile stress. (a) 12 strain works for ε variants formed in grain 1. (b) 6 strain works for α’ variants in the ε3 to α’ in grain 1. (c) 24 strain works for α’ formed in grain 2. The Euler angle for grain 1 is [318, 149, 180], and the Euler angle for grain 2 is [141, 177, 237].

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