Effect of Allotropic Transformation on Plasticity of Fe-15Mn-10Al-0.3C Dual Phase Steel during Annealing

doi:10.11901/1005.3093.2019.136

Chinese Journal of Materials Research

2019, Vol. 33

Issue (11): 837-847 DOI: 10.11901/1005.3093.2019.136

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Effect of Allotropic Transformation on Plasticity of Fe-15Mn-10Al-0.3C Dual Phase Steel during Annealing

LIU Yingkai^1,²,WANG Baibing^1,²,LIU Rendong³,GUO Jinyu³,SHI Wen^1,²(

)

1. School of Materials Science and Engineering, Shanghai University, Shanghai 200444, China
2. State Key Laboratory of Advanced Special Steel, Shanghai 200444, China
3. Technology Center of Ansteel Institute, Anshan 114009, China

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LIU Yingkai,WANG Baibing,LIU Rendong,GUO Jinyu,SHI Wen. Effect of Allotropic Transformation on Plasticity of Fe-15Mn-10Al-0.3C Dual Phase Steel during Annealing. Chinese Journal of Materials Research, 2019, 33(11): 837-847.

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Abstract

The evolution of microstructure and properties of Fe-15Mn-10Al-0.3C steel during static annealing after different cold rolling treatments was investigated. The microstructure and properties of the test steel were characterized by means of SEM, XRD and EBSD. The results show that during the annealing process, the austenite bands undergo obvious allotropic transformation, whilst γ-phase transforms to α-phase and the amount of transformation increases with annealing time. The isomeric transformation affects the tensile deformation behavior of the annealed steel, the orientation relationship between the α-phase and the γ-phase changed from the neighbor relationship to the K-S with the prolongation of annealing time, which is beneficial to dislocation sliding across phase boundary and improves plasticity. When the annealing time is long enough, the K-S relationship between the two phases loses coherent and the plasticity is reduced. The transformation can regulate the parallelism of the slip system between the α-ferrite and the γ-austenite, which can improve the plasticity of Fe-Mn-Al-C steel.

Key words: metallic materials allotropic transformation double cold rolling orientation relationship dislocation glide

Received: 01 March 2019

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	Yingkai LIU
	Baibing WANG
	Rendong LIU
	Jinyu GUO
	Wen SHI

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https://www.cjmr.org/EN/10.11901/1005.3093.2019.136 OR https://www.cjmr.org/EN/Y2019/V33/I11/837

Table 1 Chemical composition of Fe-15Mn-10Al-0.3C experimental steel (mass fraction)

Fig.1 Phase fraction in the test alloy as a function of temperature predicted by Thermo-calc software

Fig.2 Schematic illustration of the rolling and annealing condition of Fe-15Mn-10Al-0.3C steel

Fig.3 OM and SEM images of the 1030℃ isothermal for 1 h (a，b) and OM images (c, d) of the SCRS and DCRS respectively

Fig.4 Selected SEM images of the SCRS annealed at 900℃ for 1 s (a), 5 s (b), 10 s (c), 2 min (d), 10 min (e) and 1 h (f)

Fig.5 SCRS annealed at 900℃angular distribution of grain boundary (a), phase diagram (b) and IPF (c) for 1 s respectively; angular distribution of grain boundary (d), phase diagram (e) and IPF (f) for 10 s

Fig.6 Selected SEM images of the DCRS annealed at 900℃ for 5 s (a), 10 s (b), 2 min (c), 10 min (d), and 1 h (e)

Fig.7 X-ray diffraction results (a) SCRS and annealed samples; (b) DCRS and annealed samples; and Statistical map of allotropic transformation (c) Annealed after SCRS; (d) Annealed after DCRS

Fig.8 Tensile properties of selected samples quenched at 900℃ (a) Annealed after SCRS; (b) Annealed after DCRS; (c) and (d) are the work hardening rate figures of annealed specimens after single and double cold rolling

Table 2 Room temperature tensile properties of the alloy as annealed conditions

Fig.9 Austenite phase volume fraction (a) average grain size, (b) of selected samples quenched at 900℃

Fig.10 Average dislocation density increment in tensile direction of annealed specimens (a) annealed after SCRS; (b) annealed after DCRS

Fig.11 Grain orientation change of α-ferrite of annealed samples for 1 s (a) and 1 min (b) of SCRS and for 2 min (c) and 1 h (d) of DCRS

Table 3 Euler angles of α phase and γ phase at different selected locations of annealed samples

Fig.12 Degree of deviation from K-S between γ and α in annealed samples (a) and (b) are the Schematic diagram of angular distribution deviating from K-S relationship of 1 s for SCRS and 2 min for DCRS; (c) and (d) are the proportion diagrams of different ferrite slip system parallel to austenite slip system during different annealing time after SCRS and DCRS respectively; (e) and (f) are the proportion diagrams of all ferrite slip system parallel to austenite slip system during different annealing time after SCRS and DCRS

Fig.13 SEM images of microcracks at fracture of tensile samples (a) 10 s, (b) 2 min and (c) 1 h of SCRS respectively; (d) 10 s, (e) 2 min and (f) 1 h of DCRS

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