往复挤压AM60B镁合金的组织与力学性能-有色金属在线

简介概要

往复挤压AM60B镁合金的组织与力学性能

来源期刊：中国有色金属学报(英文版)2013年第11期

论文作者：王丽萍陈添姜文勇冯义成曹国剑朱岩

文章页码：3200 - 3205

Key words：magnesium alloy; cyclic extrusion compression; microstructure; mechanical properties

摘要：通过往复挤压(CEC)变形来细化AM60B镁合金的组织。结构表明：随着CEC道次的增加，组织得到明显细化。当材料达到临界最小晶粒尺寸时，进一步挤压变形也很难使组织得到明显的细化。细小的组织具有优异的力学性能，合金的硬度、屈服强度、抗拉强度和断后伸长率分别由铸态的62.3、64 MPa、201 MPa和11%上升到二道次变形后的72.2、183.7 MPa、286.3 MPa和14.0%。但是再进一步挤压变形材料的力学性能增加幅度不明显，经四道次挤压变形后其硬度、屈服强度、抗拉强度和断后伸长率分别为73.5、196 MPa、297 MPa和16%

Abstract: The cyclic extrusion compression (CEC) process was introduced into the AM60B magnesium alloy. The use of the CEC process was favorable for producing finer microstructures. The results show that the microstructure can be effectively refined with increasing the number of CEC passes. Once a critical minimum grain size was achieved, subsequent passes did not have any noticeable refining effect. As expected, the fine-grained alloy has excellent mechanical properties. The micro-hardness, yield strength, ultimate tensile strength and elongation to failure of two-pass CEC formed alloy are 72.2, 183.7 MPa, 286.3 MPa and 14.0%, but those of as-cast alloy are 62.3, 64 MPa, 201 MPa and 11%, respectively. However, there is not a clear improvement of mechanical properties with further increase in number of CEC passes in AM60B alloy. The micro-hardness, yield strength, ultimate tensile strength and elongation to failure of four-pass CEC formed alloy are 73.5, 196 MPa, 297 MPa and 16%, respectively.

Trans. Nonferrous Met. Soc. China 23(2013) 3200-3205

Microstructure and mechanical properties of AM60B magnesium alloy prepared by cyclic extrusion compression

Li-ping Wang, Tian CHEN, Wen-yong JIANG, Yi-cheng FENG, Guo-jian CAO, Yan ZHU

College of Materials Science and Engineering, Harbin University of Science and Technology, Harbin 150040, China

Received 7 February 2013; accepted 15 March 2013

Key words: magnesium alloy; cyclic extrusion compression; microstructure; mechanical properties

1 Introduction

Magnesium alloys have characteristics of low density, high specific strength and excellent machinability, attracting more and more attention [1-3]. However, their poor mechanical properties make them impossible for wide applications in electronics, automotive and aerospace industries [4,5].

Recent researches have shown that ductility of magnesium alloys at room temperature can be significantly enhanced by texture control and grain refinement treated by severe plastic deformation (SPD) processing. SPD techniques include equal channel angular extrusion (ECAE), high-pressure torsion (HPT), multi-axial forging (MAF), accumulative roll-bonding (ARB), etc [6-12]. Several researchers [13-15] have reported the SPD techniques introducing in magnesium and titanium alloys. LUO et al [13] reported the microstructure evolution of AZ91D magnesium alloy prepared by equal channel angular extrusion (ECAE). The results indicated that recrystallization first occurred in deformed areas. CHEN et al [15] integrated multi-axial forging (MAF) with a lower deformation temperature to innovate a new method to produce a fine-grained AZ61 alloy. The innovative process distinctly improved the refinement of grain size and reduced the cost. They found that the microstructure can be effectively refined with increasing equivalent strain during MAF. And temperatures decrease successively for each MAF pass. Among these SPD techniques, cyclic extrusion compression (CEC) seems to be especially attractive to overcome the in homogeneous microstructure treated by other mentioned processes due to the limited degree of deformation [16-19]. To the best of our knowledge, no studies have been reported on CEC of AM60B magnesium alloys. The present work aims to employ the CEC processes for AM60B magnesium alloy. The microstructure and mechanical properties of AM60B prepared by the CEC procedure are reported.

2 Experimental

The material used in this study was a commercial Mg-Al-Mn alloy, AM60B, and the composition was 6.2% Al, 0.31% Mn and 0.12% Zn in mass fraction, and the balanced magnesium. Billets with a diameter of 80 mm and a length of 160 mm for CEC were cut from the as-cast AM60B magnesium alloy. The CEC process made a sample within the chamber extruded repeatedly backwards and forwards. And the accumulated equivalent strain was calculated according to the following equation:

(1)

where n is the number of deformation cycles, D is the chamber diameter and d is the channel diameter. Before CEC, as-cast AM60B billets and the die were preheated at 380 °C for 60 min, and then were lubricated with molybdenum disulphide (MoS₂). A heating jacket was coated on the die and the processing temperature was controlled within ±5 °C. Subsequent work consisted of inserting the samples into the die and holding in the die for 3 min to ensure the samples to reach temperature of 380 °C. In this study, billets were extruded one pass, two passes, three passes and four passes, respectively. And the true strains of the billet treated by CEC according to equation (1) are 2.77, 5.54, 8.31 and 11.08, respectively. The samples treated by CEC were quenched in cold water when taken them out as soon as possible.

Metallographic specimens of as-cast and CEC formed alloy were ground with SiC paper of different fineness and polished with 3 μm and 1 μm diamond paste and 0.05 μm colloidal alumina. All fine grinding and polishing samples were etched in a solution of 100 mL ethanol, 6 g picric acid, 5 mL acetic acid and 10 mL water. Mechanical tensile samples with 5 mm in diameter and 60 mm in gauge length were tested using an Instron 5569 machine at a cross head speed of 1 mm/min at room temperature. Tensile curves were analyzed to assess the yield strength, ultimate tensile strength and elongation to failure. At least five measurements were tested in each condition. Hardness was measured at 1.96 N load for 20 s using a Vickers micro-hardness tester and each hardness was the average of six measurements at randomly selected points. Mean size of solid grains was calculated by intercept method.

3 Results

3.1 Microstructure

Figure 1 shows the microstructure and the XRD pattern of as-cast AM60B magnesium alloy. The microstructure of as-cast AM60B magnesium alloy is composed of α-Mg matrix and eutectic compounds, which are mainly distributed at grain boundaries. It can be seen from Fig. 1(a) that the eutectic compounds precipitate as discontinuous network at grain boundaries and some of them precipitate as particle-like inside the grains. This demonstrates that the as-cast AM60B magnesium alloy consists of α-Mg matrix and β-Mg₁₇Al₁₂ phase (Fig. 1(b)).

Fig. 1 Microstructure (a) and XRD pattern (b) of as-cast AM60B alloy

Figure 2 shows the microstructure of as-cast AM60B magnesium alloy after CEC processing one pass, two passes, three passes and four passes, respectively. Compared with the microstructure of as-cast AM60B magnesium alloy, a great number of new fine grains were observed at the initial grain boundaries in the CEC formed AM60B magnesium alloy (Fig. 2(a)), which indicates the occurrence of dynamic recrystallisation during CEC. However, the refinement of grains is initially not uniform, there are coexistence of fine and coarse grains. This is called bimodal microstructure which is caused by non-recrystallized regions of old grains and newly formed finer grains. When the number of CEC passes is increased, the area covered by fine grains increases, although a bimodal microstructure still exists (Fig. 2(b)). When the number of CEC passes is further increased, the microstructure becomes more homogeneous by successive breaking-up of coarse grains (Fig. 2(c)). However, with further CEC deformation (Fig. 2(d)), it is difficult to get further grain refinement. Figure 3 shows the grain size as a function of the equivalent strain for CEC formed AM60B magnesium alloy. As shown in Fig. 3, with the increase of equivalent strain, the mean grain size reduces progressively. Once a critical minimum grain size is achieved, subsequent passes do not have any noticeable refining effect.

Fig. 2 Microstructures of AM60B alloy after CEC

Fig. 3 Plot of grain size as function of equivalent strain

3.2 Micro-hardness and tensile properties

Figure 4 shows the micro-hardness, yield strength (YS), ultimate tensile strength (UTS) and elongation of CEC formed AM60B billets as a function of the number of CEC passes imposed on the billets. As shown in Fig. 4(a), significant improvement in micro-hardness can be obtained for CEC formed billet compared with the as-cast AM60B magnesium billet micro-hardness of 62.3. Meanwhile, the micro-hardness of the CEC formed billet is improved obviously with increasing the number of CEC passes. For instance, the hardness increases from 68.7 to 73.2 with the number of CEC passes increasing from one pass to three passes, and then it almost does not change with further increasing the number of CEC passes. Figures 4(b)-(d) indicate that the increase of the number of CEC passes improves the YS, UTS and elongation to failure. The effect of the number of CEC passes on the mechanical properties of CEC formed AM60B billets can be divided into two stages. In the first stage, the mechanical properties of CEC formed AM60B billets notably increase with increasing equivalent strain. In the second stage, the number of CEC passes has little influence on the mechanical properties of CEC formed AM60B billets.

4 Discussion

Increasing the number of CEC passes (equivalent strain) results in some changes in microstructures. For instance, a heterogeneous grained structure, which is characterized by the coexistence of fine and coarse grains, is produced after the first CEC pass. The discovery of a bimodal distribution of grain size after one pass and the nucleation of fine grains at original grain boundaries indicate that dynamic recrystallisation occurs (Fig. 2(a)) [18-20]. For dynamic recrystallisation, new strain-free grains nucleate at the original grain boundaries [21,22]. Compared Fig. 2(a) with Fig. 2(b), increasing the number of CEC passes is favorable for the formation of recrystallized grains nucleated at the boundaries of the newly formed fine grains [23,24]. The CEC process results in the distortion of crystal lattices and the accumulation of dislocations in the deformed grains, which leads to accumulation of distortion energy in the material. In this way, the materials treated by two passes have much interfacial energy than that only treated by one pass, which in turn result in the greater overall grain boundary and sub-grain boundary area. This leads to greater potential for the development of recrystallization nuclei, and results in a finer recrystallized grain size. In other words, a higher equivalent strain is that misorientation of the subgrain boundaries may increase, leading to an increase in the amount of store energy in the billet and an increased driving force towards recrystallization [25-28]. This dynamic recrystallization mechanism can also explain that the microstructure treated by CEC has a finer grain size compared with as-cast microstructure. As expected, increase in the number of CEC passes effectively improves the number of fine grains. However, the size of these fine grains is not refined further by the additional number of CEC passes. Figure 3 suggests that there is a critical equivalent strain ε_c which is in the range of 5.54-8.31 and controls the degree of the homogeneity for CEC formed AM60B magnesium alloys during their microstructure evolution process. The microstructure full of fine dynamically recrystallized grains could be got if the applied total equivalent strain ε_e exceeds the critical strain ε_c. Under this condition, it is difficult to get more grain refinement further. For dynamic recrystallization, once this process is completed, the material is in a steady state and further deformation of the material cannot change the grain size for the simply reason that larger grains provide less grain-boundary area for the nucleation of new fine grains. This means that billets with a larger initial grain size will require a higher effective strain to complete dynamic recrystallization. The Petch-Hall equation is σ_y=σ₀+K_yd^-1/2, where σ_y is the yield strength, σ₀ and K_y are material constants, and d is the mean grain size. The value of K_y, which is mainly dependent on the number of slip systems, is higher for metals with hexagonal close-packed structure (HCP) than metals with body-centered cubic (BCC) or face- centered cubic (FCC) structure. Note that magnesium alloys with HCP structure, the grain size has a significant influence on the yield strength [29,30]. As shown in Fig. 4, the increase of equivalent strain results in the improvement of mechanical properties of CEC formed billets. In this work, the solid grain size of the as-cast alloys is 132 μm. However, the solid grain size of the CEC formed alloys after four passes is 11 μm. As expected, better mechanical properties are obtained in the alloy treated by CEC. The micro-hardness, yield strength, ultimate tensile strength and elongation to failure of CEC formed alloy are 73.5, 196 MPa, 297 MPa and 16%, and 62.3, 64 MPa, 201 MPa and 11% for as-cast alloy.

Fig. 4 Curves of micro-hardness (a), yield strength (b), ultimate tensile strength (c), elongation to failure (d) vs equivalent strain

5 Conclusions

1) The CEC process is an effective route to refine coarse grains. With increasing the number of CEC passes, the microstructures of CEC processed billets are initially non-uniform with a bimodal microstructure but become more homogeneous. Once a critical minimum grain size is achieved, subsequent passes do not have any noticeable refining effect.

2) The micro-hardness, YS, UTS and elongation to failure of two-pass CEC formed alloy are 72.2, 183.7 MPa, 286.3 MPa and 14% and 62.3, 64 MPa, 201 MPa and 11% for as-cast alloy. However, there is not a clear improvement of mechanical properties with further CEC passes in AM60B alloy.

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