Microstructure comparison of ZK60 alloy under casting, twin roll casting and hot compression
WANG Shou-ren(王守仁)1, WANG Min(王 敏)2, KANG Suk-bong3, CHO Jae-hyung3
1. School of Mechanical Engineering, University of Ji’nan, Ji’nan 250022, China;
2. School of Materials Science and Engineering, Shandong University, Ji’nan 250022, China;
3. Korea Institute of Materials Science, 66 Sangnam-dong, Changwon 641010, Korea
Received 25 March 2009; accepted 4 September 2009
Abstract:
The microstructures of ZK60 alloy under conventional direct as-casting (DC), twin roll casting (TRC) and twin roll casting followed by hot compression (TRC-HC) were analyzed by optical morphology (OM), electron backscatter diffraction (EBSD) and X-ray diffraction (XRD). The deformation condition of hot compression is 350 ℃, 0.1 s-1. The microstructural evolution under TRC-HC deformation followed by annealing at different temperatures and time was discussed. The results show that TRC provides more modified microstructure compared with DC. Twins are found in TRC processing; dynamic recrystallization (DRX), shear bands and twins are found in TRC-HC. A short annealing time has little effect on hardness, while during a long time annealing, it is found that low annealing temperatures increase the micro-hardness and high temperature decreases it.
Key words:
microstructural evolution; anneal; dynamic recrystallization; static recrystallization; twin-roll casting; hot compression; magnesium alloy ZK60;
1 Introduction
Magnesium numerous elements solute to form a series of magnesium alloys which have great potential for application in lightweight structural components due to their extremely low density, high specific strength and stiffness[1-3]. Moreover, wrought Mg alloys have attracted great attention in recent years owing to their higher mechanical properties than cast Mg alloys which usually have such casting defects as porosity, inclusions as well as low ductility[4-6]. At room temperature, however, their poor workability, strong preferred crystal orientation and mechanical properties directionality of wrought Mg alloys limit their extensive application from the automotive and aerospace industries to electronic devices and consumer products. All of these shortcomings were caused by their hexagonal crystallography and lack of sufficient independent slip systems. The activations of non-basal slip system such as prismatic and pyramid plane slip at evaluated temperature result in a gradually improved formability. Diverse hot work processes such as twin-roll casting (TRC), warm rolling (WR), hot extrusion (HE), torsion straining (TS), reciprocal extrusion (RE) and equal channel angular extrusion (ECAE) are developed for the application of Mg alloys. TRC technology has such advantages as reducing several production steps in the production of strip and converting molten metals directly into an endless coiled strip suitable for cold rolling or wire-bars for wire-drawing. This technique has been developed continuously since it was first conceived by BESSEMER in 1856[7], which combines casting and hot rolling into a single step of flat rolled products. TRC processing reduces grain size and removes segregation. In addition, it saves cost due to a relatively high solidification rate ranging from 102 to 103 K/s[8]. Despite of different hot work methods, the purpose of this study is to weaken basal texture, modify microstructure, refine grains and improve the mechanical properties. Due to the strong influence of grain size on the mechanical properties, grain refinement or coarsening prevention is a promising method to enhance the strength of wrought magnesium products[9-10], and progressive deformation of post-TRC materials is necessary. JEONG and HA[11] discussed the effects of rolling conditions on the microstructure and texture development of AZ31 Mg alloy sheet; CHEN et al[12] investigated the
microstructure and mechanical properties of AZ41 alloy sheets produced by twin roll casting, sequential warm rolling and post-annealing at 350 ℃. However, the wrought materials posses high stored energy and a large fraction of non-equilibrium grain boundaries, which leads to the products non-stability in subsequent fabrication and application because of severe deformation[13-14]. Therefore, heat treatment methods were applied to induce dislocation rearrangement and accelerate the completion of recrystallization.
In the present work, the recrystallization of ZK60 alloy under TRC processing was studied. The microstructure evolutions at conventional casting (DC), twin roll casting (TRC) and hot compression (HC) were investigated. The effects of annealing on the microstructure and mechanical properties of ZK60 alloys under TRC-HC processing were discussed.
2 Experimental
Commercial magnesium alloy ZK60 was used and its chemical composition was Mg-6.20Zn-0.48Zr (mass fraction, %). The TRC processing was introduced in Ref.[15]. Uniaxial compression tests were performed with a strain rate of 0.1 s-1 at 350 ℃, the schematic diagram of the TRC-HC processing was shown in Fig.1. The specimens were quenched by nitrogen gas immediately after compression in order to prevent the microstructure from changing after deformation, then the samples were annealed at different temperatures (250-400 ℃) and time (100-50 000 s). The annealed samples were mechanically polished with polycrystalline diamond suspension glycol based solution, and subsequently etched for 7 s with a solution of picric acid (5 g), acetic acid (5 mL), distilled water (10 mL) and ethanol (100 mL). All the optical microstructures were observed along the rolling direction; the average grain size was analyzed with image analyzer, and the hardness was measured with digital microhardness tester (TOKYO, MXT70) with a load of 100 g for 15 s. X-ray diffraction (XRD) analysis was done with a D/MAX-2000 equipment (RIGAKU). Microstructural evolution and grain boundary distributions were analyzed by electron backscatter diffraction (EBSD), the specimens were prepared by both mechanical using 2000# sand paper and electro polishing operated at 11 V for 120 s in a solution of 400 mL Butyl glycol, 80 mL ethanol and 40 mL perchloric acid (HClO4) below 15 s to remove surface strain. EBSD data were acquired using a JEOL JSM-7001F field emission scanning electron microscope (FESEM) and HKL Channel 5 EBSD software (HKL Technology, Denmark). The FESEM was operated at 20 kV in high vacuum mode and the specimen was tilted at 70?.
Fig.1 Schematic diagram of TRC-HC processing
3 Results and discussion
3.1 Microstructures under different deformation condition
The optical images of ZK60 alloy deformed by DC, TRC and TRC-HC processing are shown in Fig.2. For DC, coarse and equiaxed grains (100-200 μm) and some second eutectics as well as intermetallic compounds phases along the grain boundary and the interior of the grains were observed; for TRC, lots of dendrite structures were observed, phases separated out and embedded in the interdendritic region are much finer than the initial grains; twins are found in alloy after TRC, which were examined by EBSD technique as shown in Fig.3. From orientation map, it can be seen that twins have various directions, from pole figure, the main twinning system is
86.3?
. The activation of extension twining causes a misorientation of 86.3? between the twinned and the original part of crystal. Compared with the conventional casting, TRC processing has the advantages of improvement of microstructure modification and mechanical properties, it is shown that segregations are removed, grains are refined and microstructures are homogenized in Fig.2(b). The same conclusions were deduced in Refs.[12, 16]. However, the microstructure characterizations of TRC-HC are distinctly different from that of DC and TRC. Significant microstructural changes indicated that TRC-HC processing is effective in refining grain size. From Fig.2(c), distinct bimodal structures were observed, which consist of a large number of initial and deformed grains and a small number of newly formed grains. There are dynamic recrystallization (DRX), deformation bands (shear bands) and twins in the homogeneous and initial grains. The shear bands look like long and wide “flowing rivers” which have about 37? tilting angle to the compression direction (Fig.2(c)). DRX-ed grains distribute in this “flowing rivers” while twins appear along the riverside, which results in distinct flow softening. In addition, lots of sub-structures are studded in all the “river” and “riverside”.
The XRD patterns of ZK alloys after DC, TRC and TRC-HC processing are shown in Fig.4. The data were perpendicular to the normal direction (ND). Several of the main crystal planes, (0002), 
and 
are shown in Table 1. It is shown that the orientation of DC looks like random, TRC exhibits weak preferred orientation of hexagonal crystal structure, while TRC-HC exhibits strong basal texture orientation. With the increase of deformation degree, basal plane is gradually intensified, while the intensity of non-basal plane decreases. This indicates that with the increase of deformed degree, the sample develops a strong texture, and this causes the c-axes aligned in ND resulting in progressive basal plane orientation distribution. Other peaks such as 
and
did not change distinctly, indicating that basal dislocation slips are the dominant deformation mode[17-18].
Fig.2 Optical images of ZK60 alloys under different processes: (a) DC; (b) TRC; (c) TRC-HC
Fig.3 Twins in ZK60 alloy under TRC: (a) Orientation map; (b) Pole figure
Fig.4 XRD patterns of ZK60 alloys under different deformation conditions: (a) DC; (b) TRC; (c) TRC-HC
important crystal planes, (0002),,,
and are marked. Diffracted intensities
Table 1 Diffracted intensity of main planes in alloys in Fig.4
3.2 Microstructures under different annealing conditions
EBSD Kikuchi band contrast maps for ZK60 alloys at deformation condition of 350 ℃, 0.1 s-1 and different annealing conditions are shown in Fig.5. The grey scales of band contrast maps are based on the relative intensity of the Kikuchi bands generated by the EBSD software. The dark region present the relatively low band contrast values caused by grain boundaries, particles and deformed features. The bright and white region present the occurrence of static recrystallization (SRX). It is clear that some recrystallized equiaxed grains decorate the shear bands, and elongated grains (non-shear banded materials) surround them. With the increase of annealing temperature, the amount of twins decrease while SRX grains increase; dislocations rearrange to form sub-grains. The low angle grain boundaries (LAGBs) continuously evolved into high angle grain boundaries (HAGBs), high proportions of HAGBs are consistent with high annealing temperature, while LAGBs are associated with severely deformed state as well as lower annealing temperature. Fig.6 shows the pole figure established from EBSD data for ZK60 alloys at the deformation conditions of 350 ℃, 0.1 s-1 and different annealing conditions. It is clear that the pivotal location of initial crystal orientation intensively influences the subsequent structural evolution. Under TRC-HC, the strong {0002} basal plane orientation distribution is dominant although parts of DRX grains deviate from basal plane and align to 
plane. Under annealing state, dislocation densities decrease with the increase of annealing temperature, the dark regions turn small, indicating that grain boundary turns clearer and twin boundary disappears.
Fig.5 EBSD Kikuchi band contrast maps for ZK60 alloys: (a) Unannealing; (b) 250 ℃, 1 000 s; (c) 300 ℃, 1 000 s; (d) 350 ℃, 1 000 s; (e) 400 ℃, 1 000 s
Fig.6 Pole figures established from EBSD data for ZK60 alloys (Contour levels: 1, 2, 3, 5, 7): (a) Unannealing; (b) 250 ℃, 1 000 s; (c) 300 ℃, 1 000 s; (d) 350 ℃, 1 000 s; (e) 400 ℃, 1 000 s
3.3 Microhardnesses under different annealing conditions
Fig.7 shows the microhardness (H) changes as a function of annealing time (t) at different temperatures. The H—t curves are divided into two regions (Ⅰ and Ⅱ). In Region Ⅰ, the H values have no significant changes with the increase of annealing time and temperature. In Region Ⅱ, there are two kinds of changes which can be divided into Ⅱ1 and Ⅱ2 regions. When θ＜300 ℃, there is a climbing trend with the increase of annealing time (Ⅱ2). When θ＞350 ℃, a degressive trend is obvious (Ⅱ1). This indicated that the dispersion strengthening particles improved the ability of softening resistance causing the improvement of hardness in Ⅱ2 stage, which is similar with the aging strengthening mechanism. At high temperature stage (Ⅱ1), grain size increases and the ductility improvement results in decrease of hardness H.
Fig.7 Microhardness as function of annealing time at different annealing temperature
It is well known that Hall–Petch (H-P) relationship is frequently reported to account successfully for the mechanical properties (strength and hardness) dependence of the grain size of structural element:
H=H0+kHd-n (1)
where H is the hardness; d is the average size of grains; kH and n are called H-P parameters; H0 is the initial hardness of pre-annealing. Both parameters kH and n reflect the resistance of the boundary to dislocation glide. In regard to the severe deformation ZK60 alloys of subsequent annealing time and temperature is important for SRX, that is, annealing parameters are crucial in the microstructural evolution from substructure to stable structure. Thus, n=1 is valid for sub-grain boundaries of deformed materials. Whereas overfull annealing time and super high temperature result in the growth of recrystallized grains to high angle boundaries, under this condition, n=1/2. Therefore, the H-P relationship can be described as
H=H01+kH1d-1/2 (2)
H=H02+kH2d-1 (3)
where H0 and kH are calculated by the H—d-1/2 relationship in Fig.8; kH is the slope of H-P line; kH1=80; kH2=150; H0 is the intercept; H01=69, H02=55. It can be deduced that H0 and kH are related to not only the material variety but also the deformation degree.
Fig.8 Hall–Petch relationship for ZK60 alloys
4 Conclusions
1) Twin roll casting possesses weak preferred orientation of hexagonal crystal structure while TRC-HC exhibits strong basal texture orientation. With the increase of annealing temperature, the amount of twins decreases while SRX grain increases. Dislocations rearrangement form sub-grains ultimately induced static recrystallization.
2) Different annealing conditions affect the microstructural evolution and microhardness. Shortening annealing time has a small effect on hardness. Longer time at lower annealing temperature results in the increases of the hardness, while higher annealing temperature causes the decrease of the hardness.
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(Edited by FANG Jing-hua)
Foundation item: Project(10020072) supported by the Korean Ministry of Commerce, Industry and Energy; Project(Y2008F27) supported by the Natural Science Foundation of Shandong Province, China
Corresponding author: WANG Shou-ren; Tel: +86-531-82765476; Fax: +86-0531-87108467; E-mail: sherman0158@tom.com
DOI: 10.1016/S1003-6326(09)60211-9
