Microstructural Evolution and Anisotropic Weakening Mechanism of ZK60 Magnesium Alloy Processed by Isothermal Repetitive Upsetting Extrusion

doi:10.1007/s40195-021-01293-3

Abstract

Abstract:

The isothermal repetitive upsetting extrusion (RUE) was implemented to process ZK60 magnesium alloy at 380 °C. Then, the relationship between the microstructural characters, including grain refinement and texture evolution, and the mechanical performance of the alloy was investigated. Results showed that after 3 passes of RUE, the average grain size was refined from 115.0 to 26.5 μm, which was mainly caused by the continuous dynamic recrystallization and discontinuous dynamic recrystallization. Meanwhile, the elongation of the alloy increased from 13.8 to 21.6%, and the superplasticity (142%) of the alloy has been achieved in the following high temperature tensile test, which is very beneficial for the further processing of the alloy into components. In particular, the alloy formed a distinctive texture distributed between < 2-1-11 > and < 2-1-14 > , which was greatly related to the Schmid factor of extrusion direction (ED) and transverse direction (TD). This texture changed the initiation ability of basal and prismatic slip in both directions and inhibited the initiation of partial tensile twinning in TD; thus, the anisotropy in both directions was weakened. As expected, the tensile yield strength difference decreased from 25.9 to 3.4 MPa, but it was used as the cost of tensile yield strength in ED.

Key words: Severe plastic deformation, Repetitive upsetting extrusion, ZK60 alloy, Microstructure, Mechanical properties

Zhengran Liu, Xi Zhao, Kai Chen, Siqi Wang, Xianwei Ren, Zhimin Zhang, Yong Xue. Microstructural Evolution and Anisotropic Weakening Mechanism of ZK60 Magnesium Alloy Processed by Isothermal Repetitive Upsetting Extrusion[J]. Acta Metallurgica Sinica (English Letters), 2022, 35(5): 839-852.

Figures/Tables 17

Fig. 1 Principle of repetitive upsetting extrusion: D?=?140 mm, d?=?100 mm

Fig. 2 a OM microstructure, b SEM microstructure, c XRD diffraction analysis results of ZK60 alloy after homogenization

Fig. 3 Evolution of the microstructure for increasing deformation passes: a 1 pass, b 2 passes, c 3 passes

Fig. 4 a, d, g (0001) pole figures, b, e, h crystal orientation and c, f, i inverse pole figures along ED of ZK60 alloy after different deformation passes: a-c 1 pass, d-f 2 passes, g-i 3 passes. The rightmost side shows the corresponding color indicator of the pole intensity

Fig. 5 KAM maps of ZK60 alloy after different deformation passes: a 1 pass, b 2 passes, c 3 passes; d its distribution

Fig. 6 Stress-strain curves of a ED, b TD of ZK60 alloy after different deformation passes

Table 1 Mechanical properties of ZK60 alloy after different deformation passes

Pass	ED			TD
Pass	UTS (MPa)	TYS (MPa)	Elongation (%)	UTS (MPa)	TYS (MPa)	Elongation (%)
0	272.3	159.1	13.8	-	-	-
1	277.4	167.2	16.3	280.2	141.3	15.2
2	276.1	160.9	18.2	284.7	151.5	17.7
3	275.4	153.7	21.6	286.3	157.1	21.9

Fig. 7 High temperature plasticity test samples of ZK60 alloy at 380 °C along ED after different deformation passes

Table 2 High temperature plasticity results of ZK60 alloy at 380 °C along ED after different deformation passes

Pass	0	1	2	3
Elongation	43.9%	111.9%	129.7%	142.0%

Fig. 8 EBSD orientation maps of ZK60 alloy after different deformation passes: a 1 pass, b 2 passes, c 3 passes, d corresponding misorientation angle frequency distribution

Table 3 Misorientation distribution of ZK60 alloy after different deformation passes

Pass	3°-5° (%)	5°-15° (%)	15°-180° (%)	Average (°)
1	35.73	15.17	49.10	27.58
2	20.95	12.35	66.70	36.55
3	14.95	10.58	74.47	41.76

Fig. 9 a Typical grains extracted from deformed samples (3 passes), point-to-point misorientation angle and point-to-origin misorientation angle: b A?→?B, c C?→?D

Fig. 10 a EBSD orientation map, b (0001) pole figure, and c inverse pole figure along UD of ZK60 alloy after only one upsetting; d EBSD orientation map, e (0001) pole figure and f inverse pole figure along ED after 1 pass of RUE. The rightmost side shows the color indicator corresponding to the pole intensity

Fig. 11 a, c, e, g, i, k (0001) pole figures and b, d, f, h, j, l inverse pole figures along ED of ZK60 alloy after different deformation passes: a-d 1 pass, e-h 2 passes, i-l 3 passes. Un-DRXed group displays in the left column, DRXed group displays in the right column

Fig. 12 Comparison of yield strength anisotropy between this study and other deformation magnesium alloy literature [48,49,50,51,52,53,54]

Table 4 Schmid factor of {10-10}?<?11-20?>?prismatic slip and {0001}?<?11-20?>?basal slip along ED and TD of ZK60 alloy after different deformation passes

Pass	Prismatic		Basal
Pass	ED	TD	ED	TD
1	0.285	0.349	0.351	0.313
2	0.309	0.334	0.354	0.316
3	0.325	0.326	0.355	0.323

Fig. 13 Schmid factor of {10-10}?<?11-20?>?prismatic slip along the ED of ZK60 alloy after different deformation passes: a 1 pass, b 2 passes, c 3 passes

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