Effect of Cryogenic Treatment on Mechanical Behavior of AZ31 Mg Alloy Sheet with Bimodal Non-basal Texture at Room Temperature

doi:10.11901/1005.3093.2023.555

Chinese Journal of Materials Research

2024, Vol. 38

Issue (7): 499-507 DOI: 10.11901/1005.3093.2023.555

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Effect of Cryogenic Treatment on Mechanical Behavior of AZ31 Mg Alloy Sheet with Bimodal Non-basal Texture at Room Temperature

WANG Lijia, XU Junyi, HU Li(

), MIAO Tianhu, ZHAN Sha

College of Materials Science and Engineering, Chongqing University of Technology, Chongqing 400054, China

Cite this article:

WANG Lijia, XU Junyi, HU Li, MIAO Tianhu, ZHAN Sha. Effect of Cryogenic Treatment on Mechanical Behavior of AZ31 Mg Alloy Sheet with Bimodal Non-basal Texture at Room Temperature. Chinese Journal of Materials Research, 2024, 38(7): 499-507.

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Abstract

In the present study, AZ31 Mg-alloy sheets with bimodal non-basal texture were subjected to heating treatment (520^oC/5 h), and then immediately water-quenched and quenched into liquid nitrogen for 12 h. Then, their ambient temperature mechanical performance and microstructure evolution were studied by means of uniaxial tension testing, electron backscatter diffraction (EBSD) and transmission electron microscopy (TEM). The results show that nano-precipitates Mg₁₇Al₁₂ and Al₈Mn₅ all exist in AZ31 Mg-alloy sheets. However, compared to the Mg-alloy sheet subjected to water-cooling treatment, the volume fraction and size of precipitates increase about 65.5% and 78.7% respectively for the sheet subjected to cryogenic treatment. Meanwhile, the volume fraction of { $10 1 ¯ 2$ } extension twin (ET) increases by 38.0% and 36.7% for the sheet being subjected to 6% and 12% deformation, respectively. The yield strength (YS) and ultimate tensile strength (UTS) of the cryogenic treated sheets are increased by 43.8% and 5.2%, respectively, compared with the water-cooling treated ones, however, the fracture elongation (FE) decreases by 20.4%. The increase in YS and UTS may mainly be due to the generation of high-density dislocations and precipitation strengthening by Mg₁₇Al₁₂ and Al₈Mn₅ precipitates during cryogenic treatment. The decrease in FE is mainly due to the accumulation of high-density dislocations near { $10 1 ¯ 2$ } ET boundaries during tensile deformation at room temperature, which would hinder the movement of basal slip and benefit in propagation of microcracks to expand to this region.

Key words: metallic materials non-basal texture AZ31 magnesium alloy cryogenic treatment microstructure evolution plastic deformation mechanism

Received: 22 November 2023

ZTFLH:

TG146.22

Fund: Special Funded Project of Chongqing Postdoctoral Research Program(2021XM1022);Science and Technology Research Program of Chongqing Municipal Education Commission(KJQN202101141);Cultivation Plan of Scientific Research and Innovation Team of Chongqing University of Technology(2023TDZ010);Postgraduate Innovation Project of Chongqing University of Technology(gzlcx20222004);Student Innovation and Entrepreneurship Training Program Project of Chongqing University of Technology(202311660005)

Corresponding Authors: HU Li, Tel: 17358428920, E-mail: huli@cqut.edu.cn

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	WANG Lijia
	XU Junyi
	HU Li
	MIAO Tianhu
	ZHAN Sha

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https://www.cjmr.org/EN/10.11901/1005.3093.2023.555 OR https://www.cjmr.org/EN/Y2024/V38/I7/499

Fig.1 Initial microstructure and texture of fabricated AZ31 Mg alloy sheet (a) inverse pole figure (IPF) (b) statistical analysis of grain size (c) (0002) (11 $2 ¯$ 0) (10 $1 ¯$ 0) pole figures (PFs)

Fig.2 True stress-strain curves (a) and working hardening curves (b) of CT and WQ samples

Table 1 Mechanical properties of CT and WQ samples during uniaxial tension

Fig.3 Microstructure analysis of CT sample at deformation degree of 6% and 12% (a, d) Inverse pole figure (IPF) maps; (b, e) Grain boundaries (GBs) maps; (c, f) Kernel average misorientation (KAM) maps

Fig.4 Misorientation angle distribution of CT sample during tensile deformation

Fig.5 IPF maps and (0002) PF maps of selected {10 $1 ¯$ 2} ETs in 6%-deformed (a~c) and 12%-deformed (d~f) CT samples

Fig.6 TEM images of WQ sample (a~f) and CT sample (g~l)

Fig.7 TEM micrographs of 6%-deformed CT sample (a, c, d) BF images of different regions (b) HRTEM image of selected region in Fig.7a

Fig.8 Schematic diagram of involved deformation mechanisms during uniaxial tension deformation of WQ (a) and CT (b) samples

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