High mechanical properties of rolled ZK60 mg alloy through pre-equal channel angular pressing.

Yuan, Yuchun ; Ma, Aibin ; Jiang, Jinghua 等

1. Introduction

Magnesium alloy is considered as a promising structure material for its low density and high specific strength [1]. However, the hexagonal close-packed crystal structure of Mg alloy provides limited slip systems which usually results in poor ductility and formability at ambient temperature. In addition, because the critical resolved shear stresses(CRSS) of the basal slip is significantly lower than those of other slip systems and twinning mode at low temperature [2], strong deformation anisotropy generally develops during the forming process [2, 3] that directly affects its workability. Basal texture (the basal plan paralleled the rolling plane) usually formed during rolling [4, 5], which makes further rolling difficult and leads to poor ductility and inadequate strength of the rolled sheet. Therefore, how to avoid or weaken the rolling basal texture become important for improving the formability and mechanical property of the rolling magnesium alloy sheet. Differential speed rolling or rolling at high temperature could weaken the basal texture [6, 7], and thus improved the plasticity of the magnesium alloy sheets, but the strength still cannot be increased distinctly.

Equal channel angular pressing (ECAP) [8, 9] as a common severe plastic deformation (SPD) method could refine the grains of the magnesium alloy and improve its ductility notably [10, 11]. The specific texture of ECAP [3, 10] played a great role in the good ductility and relatively low yield strength. Therefore, when ECAP was carried out before rolling, the fine microstructure and good ductility of the alloy would help for both of the rolling formability and mechanical properties.

2. Experimental procedures

The alloy used in this study was ZK60 with a composition of Mg-6.08wt% Zn-0.56wt% Zr. The ingot ZK60 alloy sample(20 mm x 20 mm *45 mm) was first solution treated at 430[degrees]C for 16 h and ECAP processed (ECAPed) for 12 passes at 300[degrees]C by a rotational die ECAP setup [12]. Before rolling, the ECAPed sample was cut paralleling to the flow plane (X-Y shown in Fig. 1, a into 5mm thick thin plates. Then these plates were rolled at room temperature (~25[degrees]C) and 150[degrees]C. The plate was annealed at 380[degrees]C for 0.5 h firstly to relax the residual strain before rolling at room temperature, and then rolled for multi passes until a total 30% reduction before fracture. When the plate was rolled at warm temperature, the plate was annealed at 300[degrees]C for 15 minutes before rolling, and between two rolling passes, it was re-annealed to 300[degrees]C for 5 minutes. The roller was kept at 150[degrees]C during the whole rolling process. The total rolling strain was up to 80% without cracks. For comparison, the solution treated ZK60 alloy was subjected to rolling alone at 150[degrees]C up to 40% rolling strain. Between two rolling passes, the plate was also annealed at 300[degrees]C for 5 minutes.

The microstructures of the ZK60 samples at different processing states were observed by optical microscopy (OM) and transmission electron microscopy (TEM). Acetic-picrate solution (3 g picric, 20 ml acetic acid, 20 ml water, and 50 ml ethanol) was adopted for etching. The TEM specimens were prepared using jet polishing with a solution of 2% perchloric acid in ethanol at -20[degrees]C. Tensile tests were carried out at room temperature with a strain rate of 5 x 10-4 [s.sup.-1]. Dog-bone specimen as demonstrated in Fig. 1, a was used with the dimension of 1.0 mm thick, 2.0 mm wide and 6 mm in gage length. The texture evolution was explored by EBSD in the flow or rolling plane (X-Y), Fig. 1, a. In order to improve the surface quality, the EBSD samples were electro-polished in a 4:1 solution of ethanol and [H.sub.3]P[O.sub.4] after mechanical polishing

3. Results and discussion

Fig. 1, a shows the process procedure at present study. The typical tensile stress-strain curves of the ZK60 samples at different processing states were exhibited in Fig. 1, b. Both of the strength and ductility of the rolled samples with pre-ECAP processing were higher than the rolled alone sample. The strengths were also much higher than the ECAPed sample. The combination of ECAP and cold rolling yielded the highest yield strength (YS) and ultimate strength (UTS), 396 MPa and 430 Mpa, with 9.4% of the elongation to failure. The YS was up to two-fold of that of the ECAPed sample. When rolling at 150[degrees]C, the rolling strain was up to 80% without any visible cracks, as the inset shown in Fig. 1, a, which was only 40% in the traditional warm rolling. Therefore, the good ductilit of the ECAPed alloy helped for improving the rolling formability at low temperature. Although the ductility of the rolled alloy decreased comparing to the ECAPed alone sample, both of the YS and UTS were enhanced significantly.

Pre-ECAP was demonstrated useful to enhance the rolling formability and mechanical properties of the ZK60 magnesium alloy. Fig. 2 shows the relevant microstructure evolution of the alloy with the operated processes. The solution treated ZK60 alloy had an equiaxed grain structure with the grain size of ~200 [micro]m. After rolling alone, the grains were refined to ~18 [micro]m. Because the rolling temperature was low, many twins could be seen inside the grains. The grains were refined to ~7 [micro]m by ECAP. Due to the dynamic recrytallization, the twin density in the ECAPed alloy sample was lower than that in the rolled alone sample. When the sample was rolled at room temperature after ECAP, as shown in Fig. 2, d, the gains were further refined. Some superfine grains were hardly identified in the optical photograph. Through the TEM micrograph of the sample rolled at room temperature, Fig. 3, b, it could be seen clearly that the grains is finer than that of the ECAPed sample. The grains size was only ~1 [micro]m. Dynamic recrystallization happened during rolling even at room temperature. High density of dislocations could be seen in the ECAPed and rolled sample, Fig. 3, c. Twins could also be seen in some big grains in Fig. 2, d, but in the TEM micrograph Fig. 3, c, the twin density was not very high. The twin boundaries degraded and changed into subgrain/grain boundaries accompanying with the dynamic recrystallization. The superfine grain size improved the compatibility of deformation that helped for both of the strength and ductility. And the improved grain boundaries and dislocations undoubtedly improved the strength of the ECAPed and rolled alloy.

[FIGURE 1 OMITTED]

[FIGURE 2 OMITTED]

When the ECAPed sample was rolled and annealed at higher temperature, 150[degrees]C and 300[degrees]C respectively, recrystallization took place and developed quickly. The average grain size was higher than that in the sample rolled at room temperature, as shown in Fig. 2, e. In addition, a large number of parallel twins could be seen inside the grains. Therefore, although the rolling strain was higher when rolling and annealing at higher temperature, the strength and ductility were lower.

Due to the great deformation anisotropy in magnesium alloys, the influence of the deformation texture in the mechanical properties cannot be ignored. The {0001}, {1010} pole figures and the inverse pole figures of the normal direction (ND) of the samples at different deformation state were studied by EBSD and exhibited in Fig. 3. The rolled alone sample showed a distinct but not very strong basal texture, as shown in Fig. 3, a. In addition to the basal texture, there was another preferred orientation that < 21 11l > nearly paralleled to the ND. Because the rolling temperature was only 150[degrees]C, twinning as the dominated deformation mode to coordinate the dislocation slip partially changed the deformation texture. The {10 [bar.1]2} < [bar.1]011 > tension twinning and {10 [bar.1]1} < [bar.1]012 > compression twinning are the two most common twinning mechanisms in magnesium alloy [13]. When rolling at low temperature, once the basal texture formed, the tension twinning was hard to happen due to most of the grains are subjected to compression in the c axis. However, compression twinning was more stabilized and harder to migrate than the tension twinning [14].Therefore, the ductility and formability of the rolled alone sample was very poor.

[FIGURE 3 OMITTED]

After ECAP processing, the basal planes in most grains preferred to incline to the ND and RD with an angle, as shown in Fig. 4, b, and < 2[bar.1][bar.1]1 > close to paralleled to ND. By subsequent rolling at room temperature with 30% reduction, a large number of dislocations and twins could be activated easily due to the favorable initial texture. Some of the basal planes rotated to parallel to the rolling direction, and the basal pole paralleled to the TD. Only a few of the basal plans rotated toward the rolling plane. The basal texture formation was impeded by the initial ECAP-texture. When rolling was conducted with a higher strain (80%) at 150[degrees]C, the texture trended to change in two ways. Some of the basal planes rotated ~ 60[degrees] to be symmetrically distributed to the initial texture, and some basal planes rotated toward the rolling plan. More twins were activated by the large compact deformation in the thickness. However, even by the 80% rolling strain, the maximum pole density of {0001} was much lower than that of the rolled alone sample. The texture change accompanying with the big grains and high density of deformation defects led to the lower strength and ductility.

[FIGURE 4 OMITTED]

4. Conclusions

Enhanced mechanical properties have been achieved in the rolled ZK60 Mg alloy sheet by pre-ECAP processing. The fine microstructure and specific texture of the ECAPed alloy led to the good rolling formability of the ZK60 Mg alloy at low temperature. During the subsequent rolling, the grains was further refined and the dislocations increased, which effectively improved the work hardening and the strength. The fine microstructure and non-basal texture facilitated the good ductility.

Acknowledgements

This work is financially supported by National Natural Science Foundation of China (Grant No. 51141002), Natural Science Foundation of Jiangsu Province of China (Grant No. BK20131373), and Jiangsu Planned Projects for Postdoctoral Research Funds (Grant No. 1402009A).

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Received September 15, 2015

Accepted July 04, 2016

Yuchun Yuan, Hohai University, Nanjing 210098, China, E-mail: yychehai@163.com

Aibin Ma, Hohai University, Nanjing 210098, China, E-mail: aibin-ma@hhu.edu.cn

Jinghua Jiang, Hohai University, Nanjing 210098, China, E-mail: jinghua-jiang@hhu.edu.cn

Xiaofan Gou, Hohai University, Nanjing 210098, China, E-mail: xfgou@hhu.edu.cn

Dan Song, Hohai University, Nanjing 210098, China, E-mail: songdancharls@hhu.edu.cn

Donghui Yang, Hohai University, Nanjing 210098, China, E-mail: yang_donghui76@hotmail.com

Weiwei Jian, North Carolina State University, Raleigh, NC 27695, USA, E-mail: wjian@ncsu.edu

http://dx.doi.org/10.5755/j01.mech.22.4.16161