Deformation-induced martensitic transformation kinetics and correlative micromechanical behavior of medium-Mn transformation-induced plasticity steel

doi:10.1016/j.jmst.2019.04.007

Abstract

Abstract:

An in situ high-energy X-ray diffraction (HE-XRD) technique was mainly used to investigate the micromechanical behavior of medium-Mn Fe-0.12C-10.16Mn-1.87Al (in wt%) transformation-induced plasticity (TRIP) steel subjected to intercritical annealing at 625 °C, 650 °C, 675 °C and 700 °C for 1 h. As the intercritical annealing temperature increased, the volume fraction of retained austenite (RA) and ultimate tensile stress (UTS) increased, while the Lüders strain and yield stress (YS) decreased. The incremental work-hardening exponent of experimental steel increased with increasing intercritical annealing temperature. The overall trend of the transformation kinetics of the RA with respect to the true strain followed the sigmoidal shape predicted by the Olson and Cohen (OC) model. Load partitioning occurred among the ferrite, austenite and martensite immediately after entering the yielding stage. Because the stability of the RA decreased with increasing intercritical annealing temperature, the load undertaken by the martensite increased. The moderate transformation kinetics of the RA and effective load partitioning among constituent phases were found to contribute to a favorable combination of strength and ductility for this medium-Mn TRIP steel.

Key words: Medium-Mn TRIP steel, High-energy X-ray diffraction, Transformation kinetics, Load partitioning

Minghe Zhang, Haiyang Chen, Youkang Wang, Shengjie Wang, Runguang Li, Shilei Li, Yan-Dong Wang. Deformation-induced martensitic transformation kinetics and correlative micromechanical behavior of medium-Mn transformation-induced plasticity steel[J]. J. Mater. Sci. Technol., 2019, 35(8): 1779-1786.

Figures/Tables 13

Fig. 1. Experimental configuration of the tensile test with in situ synchrotron-based HE-XRD experiments.

Fig. 2. SEM micrographs of Fe-0.12C-10.16Mn-1.87Al steel subjected to intercritical annealing at different temperatures: (a) 625 °C, (b) 650 °C, (c) 675 °C and (d) 700 °C.

Fig. 3. Engineering stress-strain curves of Fe-0.12C-10.16Mn-1.87Al steel tested during in situ HE-XRD experiments at room temperature.

Table 1 Mechanical properties of Fe-0.12C-10.16Mn-1.87Al steel subjected to intercritical annealing at different temperatures.

Specimen	YS (MPa)	UTS (MPa)	TE (%)	UTS × TE (GPa%)
IA625 IA650	1058 964	1099 1163	26.6 44.8	29.2 52.1
IA675	820	1330	31.1	41.2
IA700	394	1420	18.2	25.8

Fig. 4. (a) True stress-true strain curves of Fe-0.12C-10.16Mn-1.87Al steel; (b) Incremental work-hardening exponent nincr of Fe-0.12C-10.16Mn-1.87Al steel as a function of true strain.

Fig. 5. (a) XRD patterns of the undeformed samples; (b) XRD patterns of the fractured samples; (c) evolution of the volume fraction of RA as a function of engineering strain for the Fe-0.12C-10.16Mn-1.87Al steel.

Fig. 6. Normalized austenite transformed fraction of Fe-0.12C-10.16Mn-1.87Al steel during tensile deformation: (a) IA625 and IA650, (b) IA675 and IA700.

Table 2 Parameters α and β for Fe-0.12C-10.16Mn-1.87Al steel.

Sample	α	β	m
IA625	8.85117	0.13425	2
IA650	4.84323	1.18125	2
IA675	7.59199	2.03929	2
IA700	29.33865	1.75375	2

Fig. 7. Martensite transformation rate for Fe-0.12C-10.16Mn-1.87Al steel as a function of true strain.

Fig. 8. The {211} diffraction peaks of IA675 sample (a) diffraction patterns of α-211 and α'-211 deformed at an engineering strain of 0.15; (b) diffraction patterns of α-211 and α'-211 deformed at an engineering strain of 0.24.

Table 3 Elastic modulus (GPa) and Poisson's ratio for individual (hkl) planes.

Sample	E_α-211	ν _α-211	E_γ-311	ν _γ-311
IA625	192	0.22	197	0.25
IA650	186	0.24	196	0.28
IA675 IA700	185 157	0.24 0.25	190 162	0.28 0.31

Fig. 9. Lattice strains for reflections from constituent phases along the LD and TD as a function of true strain: (a) IA625, (b) IA650, (c) IA675 and (d) IA700.

Fig. 10. Phase stress of constituent phases as a function of true strain during deformation: (a) IA625, (b) IA650, (c) IA675 and (d) IA700.

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