Investigation of Portevin-Le Chatelier effect in rolled α-phase Mg-Li alloy during tensile and compressive deformation

doi:10.1016/j.jmst.2020.04.022

Abstract

Abstract:

Avoiding the Portevin-Le Chatelier (PLC) effect is very important concern for wrought Mg-Li alloys. In this study, the special PLC effect was found in rolled Mg-5Li-3Al-2Zn (LAZ532) alloy during tensile and compressive deformation. By observing microstructure evolution of the alloy during tensile and compressive deformation, it was found that prismatic <a> and pyramidal <c + a> slips were activated during tensile deformation, resulting in plenty of dislocation accumulation. In the deformation process after compressive yielding, the deformations in coarse grains and fine grains were dominated by {10 $\bar{1}$ 2} extension twinning and grain boundary slip, respectively. Based on experimental result analysis, the sudden appearance of PLC effect in the later stage of axial tensile deformation (along rolled direction) was caused by interaction between solute atoms and dislocations. In the process of axial compressive deformation (along rolled direction), PLC effect presented the complex and changeable phenomenon of appeared-disappeared-appeared, which was mainly caused by the continuous nucleation of twin in the material, the activation of grain boundary slip and the shear deformation of twin, respectively.

Key words: Mg-Li alloy, Portevin-Le Chatelier effect, Dynamic strain aging, Twins

Xiaoqiang Li, Chunlong Cheng, Qichi Le, Lei Bao, Peipeng Jin, Ping Wang, Liang Ren, Hang Wang, Xiong Zhou, Chenglu Hu. Investigation of Portevin-Le Chatelier effect in rolled α-phase Mg-Li alloy during tensile and compressive deformation[J]. J. Mater. Sci. Technol., 2020, 52: 152-161.

Figures/Tables 11

Fig. 1. Mechanical properties of LAZ532 alloys at different rolling passes: (a) tensile properties; (b) compressive properties.

Fig. 2. Distribution of amplitudes of stress fluctuations for LAZ532 alloys at different rolling passes: (a) the range from 16% to 18% tensile strain; (b) the range from 16% to 20% compressive strain.

Fig. 3. EBSD images and inverse pole figures of LAZ532 alloy rolled 9 passes during tensile and compressive deformation: (a, b) initial state; (c, d) 6% tensile strain; (e, f) 17% tensile strain; (g, h) 6% compressive strain.

Fig. 4. Twins and misorientation distribution maps of LAZ532 alloy rolled 9 passes during tensile and compressive deformation: (a, b) 6% tensile strain; (c, d) 17% tensile strain; (e, f) 6% compressive strain.

Fig. 5. (a) EBSD image and (b) pole figures of fine grains and twinning areas of LAZ532 alloy rolled 9 passes at 6% compressive strain, and (c, d) EBSD maps of corresponding pole density points (black circles).

Fig. 6. In-situ SEM maps of LAZ532 alloy rolled 9 passes during compressive deformation: (a) initial state; (b) 5% strain; (c) 10% strain; (d) 13% strain.

Fig. 7. Local misorientation maps and local misorientation angle distribution maps of LAZ532 alloy rolled 9 passes during tensile and compressive deformation: (a, b) initial state; (c, d) 6% tensile strain; (e, f) 17% tensile strain; (g, h) 6% compressive strain.

Fig. 8. Calculated mean GND density distributions of LAZ532 alloy rolled 9 passes during tensile and compressive deformation: (a) initial state; (b) 6% tensile strain; (c) 17% tensile strain; (d) 6% compressive strain.

Fig. 9. Schmid factor (SF) distribution maps of Mg-5Li-3Al-2Zn alloy rolled 9 passes during tensile deformation: (a) initial state; (b) 6% tensile strain; (c) 17% tensile strain; (d) average SF values of each slip system under different strain.

Fig. 10. TEM maps of LAZ532 alloy rolled 9 passes at 17% tensile strain: (a, b) two-beam dark-field images taken along the [0001] zone axis under g = (1- 2 $\bar{1}$ 0) and g = (01 $\bar{1}$ 0), respectively; (c, d) two-beam dark-field images taken along the [1 $\bar{2}$1 $\bar{1}$] zone axis under g = (0 $\bar{1}$ 11) and g = (10 $\bar{1}$ 0), respectively.

Fig. 11. (a) Schematic diagram of solute atoms, (b) {0001}<11 $\bar{2}$ 0> slip system, (c) schematic illustration of the grain rotation mechanisms during deformation and (d) the dynamic strain aging model.

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