Effects of minor Sr, Sn and Sc addition on as-cast microstructure and mechanical properties of ZA84 magnesium alloy
YANG Ming-bo(杨明波)1, 2, ZHU Yi(朱 翊)1, PAN Fu-sheng(潘复生)2, YANG Hui(杨 惠)1
1. Materials Science and Engineering College, Chongqing University of Technology, Chongqing 400050, China;
2. National Engineering Research Center for Magnesium Alloys, Chongqing University, Chongqing 400030, China
Received 23 September 2009; accepted 30 January 2010
Abstract: The effects of minor Sr, Sn and Sc addition on the as-cast microstructure and mechanical properties of the ZA84 magnesium alloy were compared. The results indicate that addition of 0.1%Sr, 0.5%Sn or 0.3%Sc (mass fraction) to the ZA84 alloy can refine the grains of the alloy. Furthermore, addition of 0.1%Sr to the ZA84 alloy does not obviously change the morphology and distribution of Mg32(Al,Zn)49 phase. However, addition of 0.5%Sn or 0.3%Sc not only refines and modifies the Mg32(Al,Zn)49 phase but also suppresses the formation of Mg32(Al,Zn)49 phase, especially with the addition of 0.3%Sc. Furthermore, addition of 0.1%Sr, 0.5%Sn or 0.3%Sc to the ZA84 alloy improves the tensile properties at room temperature and 150 ?C, especially with the addition of 0.1%Sr and 0.3%Sc. However, addition of 0.1%Sr is not beneficial to the creep properties, and addition of 0.5%Sn has no obvious influence on the creep properties. Oppositely, addition of 0.3%Sc to the ZA84 alloy greatly improves the creep properties.
Key words: magnesium alloy; ZA84 magnesium alloy; Sr; Sn; Sc
1 Introduction
Magnesium alloys are the lightest commercially available structural materials and have great potential for applications in automotive, aerospace and other industries. In recent years, improving the elevated temperature properties has become a critical issue for possible application of magnesium alloys in hot components. It was reported that the ZA84 (Mg-8Zn-4Al) alloy of the ZA (Mg-Zn-Al) system is a potential magnesium alloy due to its moderate mechanical properties and good creep resistance, which satisfies the requirement of corrosion resistance properties as compared with AZ91 alloy[1-4]. However, the castability and elevated temperature mechanical properties of the ZA84 alloy are not completely satisfying, and further enhancement in the properties for the alloy needs to be considered by alloying and/or micro-alloying. WANG et al[5] found that RE addition to the ZA84 alloy can modify the morphology, chemical compositions and stability of the precipitates and thus enhance the properties. However, RE addition to the ZA84 alloy possibly decreases the casting fluidity due to an increase of solidification temperature range[5]. In addition, BALASUBRAMANI et al[6] reported that Sb addition to the ZA84 alloy can refine the Mg32(Al,Zn)49 phase besides forming Mg3Sb2 precipitate and has a little effect on the grain refinement. Strength at both room and elevated temperatures are found to increase in Sb added alloys with slight reduction in ductility. Although the above studies have been carried out to understand the effects of alloying and/or micro-alloying in the ZA84 alloy, the effects of other alloying and/or micro-alloying elements such as Sr[7-10], Sn[7,11-12] and Sc[13-14], all of which have been successfully used to improve the mechanical properties of other magnesium alloys, have not been investigated. The present work aims to investigate and compare the effects of minor Sr, Sn and Sc addition on the as-cast microstructure and mechanical properties of the ZA84 magnesium alloy.
2 Experimental
The experimental alloys were prepared from pure Mg, Al, Zn and Sn (>99.9%), Mg-10%Sr and Mg-2.91%Sc (mass fraction) master alloys. In addition, Mn was added in the form of Mg-4.38%Mn (mass fraction) master alloy to decrease the iron content. The experimental alloys were melted in a crucible resistance furnace with flux protection. After being homogenized by mechanical stirring at 740 ?C and mixed completely, the melt was held at 740 ?C for 20 min and then poured into a permanent mould to obtain a casting. The tensile and creep specimens with a size reported in Ref.[10] were fabricated by wire-electrode cutting from the casting. Table 1 lists the actual chemical compositions of the experimental alloys.
Table 1 Compositions of experimental alloys (mass fraction, %)
The samples were etched in an 8% nitric acid distilled water solution, and then examined by an Olympus optical microscope (OM) and JEOL/ JSM-6460LV type scanning electron microscope (SEM) equipped with an Oxford energy dispersive spectrometer (EDS). The phases in the as-cast experimental alloys were analyzed by D/Max-1200X type X-ray diffractometer (XRD) operated at 40 kV and 30 mA. The tensile properties of the as-cast experimental alloys at room temperature and 150 ?C were determined from a stress—strain curve. The ultimate tensile strength (UTS), 0.2% yield strength (YS) and elongation to failure were obtained based on the average of three tests. The constant-load tensile creep tests of the as-cast experimental alloys were performed at 150 ?C and 50 MPa for 100 h. The total creep strain and minimum creep rates of the experimental alloys were measured from each elongation versus time curve.
3 Results and discussion
3.1 Comparison of as-cast microstructures
Fig.1 shows the XRD patterns of the as-cast experimental alloys. In general, in the ZA84 alloy, two main ternary phases are reported in Ref.[15]. One is identified as Mg32(Al,Zn)49, and the other is Mg5Zn2Al2 phase. As shown in Fig.1, all the as-cast experimental alloys are mainly composed of a-Mg, Mg32(Al,Zn)49 and Mg5Zn2Al2 phases. Furthermore, it is found that adding 0.5%Sn to the ZA84 alloy results in the formation of Mg2Sn. However, adding 0.1%Sr and 0.3%Sc to the ZA84 alloy do not cause the formation of any new phase in the alloy.
Fig.1 XRD patterns of as-cast experimental alloys
Figs.2 and 3 show the optical and SEM images of the as-cast alloys, respectively. It is found from Fig.2 that adding 0.1%Sr, 0.5%Sn or 0.3%Sc to the ZA84 alloy seems to refine the grains of the alloy. Furthermore, it is found that two types of phases showing different morphologies are present in the as-cast alloys. One is continuous and/or quasi-continuous network which mainly distributes at the grain boundaries, and the other is in an isolated shape. According to the XRD and EDS results, the continuous and/or quasi-continuous precipitates are Mg32(Al,Zn)49, and the isolated phases is Mg5Zn2Al2. In addition, as shown in Fig.3(d), some relatively fine particles mainly contained Mg, Al, Sc and Mn are observed in the Sc-containing alloy although no Sc-containing phases are detected in the XRD results.
In addition, it is observed from Fig.3 that adding 0.1%Sr to the ZA84 alloy does not obviously influence the morphology and amount of the Mg32(Al,Zn)49 phase. However, after adding 0.5%Sn and 0.3%Sc to the ZA84 alloy, especially after adding 0.3%Sc, the morphology of the Mg32(Al,Zn)49 phase gradually changes from coarse continuous and/or quasi-continuous net to relatively fine quasi-continuous and/or disconnected shape, and the amount of the Mg32(Al,Zn)49 phase obviously decreases.
3.2 Comparison of mechanical properties
The tensile properties, including ultimate tensile strength (UTS), 0.2% yield strength (YS), elongation, and creep properties of the as-cast experimental alloys are listed in Table 2. It is observed that the tensile properties of the 2#-4# alloys at room temperature and
Fig.2 Optical images of as-cast alloys: (a) 1#; (b) 2#; (c) 3#; (d) 4#
Fig.3 SEM images of as-cast alloys: (a) 1#; (b) 2#; (c) 3#; (d) 4#
150 ?C are higher than those of the 1# alloy, indicating that adding 0.1%Sr, 0.5%Sn and 0.3%Sc to the ZA84 alloy can improve both the tensile strength and elongation of the alloy. This situation is possibly related to the effects of Sr, Sn and Sc additions on the as-cast microstructure of the ZA84 alloy. Furthermore, it is observed from Table 2 that among the Sr-, Sn- and Sc-containing ZA84 alloys, the tensile properties of the Sr- and Sc-containing alloys at room temperature and 150 ?C are relatively high. In addition, it is observed from Table 2 that the 4# alloy exhibits higher creep properties than the 1# alloy while the creep properties of the 2# alloy are lower than those of the 1# alloy, and the creep properties of the 3# alloy are similar to those of the 1# alloy. The above results indicate that adding 0.1%Sr to the ZA84 alloy is not beneficial to the creep properties of
Table 2 Tensile and creep properties of as-cast experimental alloys
the alloy, and adding 0.5%Sn to the ZA84 alloy has no obvious influence on the creep properties of the alloy. However, adding 0.3%Sc to the ZA84 alloy can greatly improve the creep properties of the alloy. At present, the reason for the difference of the effects of minor Sr, Sn and Sc additions on the creep properties of the ZA84 alloy is not clear. Further investigation still needs to be considered.
3.3 Discussion
The above results indicate that adding 0.1%Sr, 0.5%Sn or 0.3%Sc to the ZA84 alloy can effectively refine the grains of the alloy. In addition, adding 0.5%Sn or 0.3%Sc to the ZA84 alloy can also modify and refine the Mg32(Al,Zn)49 phase in the alloy. In general, the grain refinement in industrial applications usually involves adding nucleates and/or solute elements into a melt before casting, and the effect of a solute element is explained in terms of the growth restriction factor (GRF) [16]. According to the GRF mechanism, the larger the GRF value is, the higher the refinement efficiency of a solute element is. Obviously, the grain refinement of the ZA84 alloy added with 0.1%Sr can easily explained by the GRF mechanism. Furthermore, the reason for the refinement and/or modification of grains and Mg32(Al,Zn)49 phases in the ZA84 alloy added with 0.5%Sn is possibly related to the Sn enrichment of the liquid during solidification, which induces a constitution undercooling at the solidification interface front. Of course, it is one of the possible reasons that the Mg2Sn compound which has high thermal stability possibly inhibits the growth of grains and Mg32(Al,Zn)49 phases during solidification. In addition, the reason for the refinement and/or modification of grains and Mg32(Al,Zn)49 phases in the ZA84 alloy added with 0.3%Sc is possibly related to the Sc enrichment. It is well known that Sc atom has larger atomic radius than Al and Zn atoms. After the addition of Sc to the ZA84 alloy, the Sc element is rich in the solid/liquid interface during solidification, and the enrichment hinders the diffusion of Zn and Al atoms and induces the constitution undercooling at the solidification interface front. Accordingly, the grains and Mg32(Al,Zn)49 phase are refined.
In addition, the above results indicate that adding 0.1%Sr to the ZA84 alloy has no obvious influence on the amount of the Mg32(Al,Zn)49 phase in the alloy. However, after adding 0.5%Sn or 0.3%Sc to the ZA84 alloy, especially after adding 0.3%Sc, the amount of the Mg32(Al,Zn)49 phase is obviously decreased, indicating that adding minor Sn or Sc to the ZA84 alloy can suppress the formation of Mg32(Al,Zn)49 phase. Based on the Mg-Zn-Al phase diagram and the investigation of ZHANG et al[17], during the solidification of Mg-Zn-Al alloys, the primary α-Mg phases first nucleate and grow until the temperature reaches about 343 ?C, where a binary eutectic reaction L1→α-Mg+Mg5Zn2Al2 occurs followed by a ternary quasi-peritectic reaction L2+ Mg5Zn2Al2→α-Mg+Mg32(Al,Zn)49. Finally, the binary eutectic reaction L3→α-Mg+Mg32(Al,Zn)49 takes place. In this case, if the amount of Mg5Zn2Al2 phase was relatively large, it would not be used up in the ternary quasi-peritectic reaction. Accordingly, the final microstructure consists of α-Mg, Mg32(Al,Zn)49 and Mg5Zn2Al2 phases as the studied ZA84 alloys in this work. Therefore, it is inferred that the decrease of the amount for the Mg32(Al,Zn)49 phase in the Sn- and Sc-containing ZA84 alloys might be related to the effects of Sn and Sc additions on the eutectic reaction of the ZA84 alloy during solidification. In spite of the above analysis, the reason for the effects of Sr, Sn and Sc additions on the amount of the Mg32(Al,Zn)49 phase in the ZA84 alloy is not completely clear. Further investigation needs to be considered.
4 Conclusions
1) The difference for the effects of minor Sr, Sn and Sc addition on the as-cast microstructure of the ZA84 alloy is relatively obvious. Adding 0.5%Sn to the ZA84 alloy results in the formation of Mg2Sn, while adding 0.1%Sr or 0.3%Sc to the ZA84 alloy does not cause the formation of any new phase in the alloy. Furthermore, adding 0.1%Sr, 0.5%Sn or 0.3%Sc to the ZA84 alloy can refine the grains of the alloy, and adding 0.1%Sr has no obvious influence on the morphology and amount of the Mg32(Al,Zn)49 phase in the alloy. However, after adding 0.5%Sn or 0.3%Sc to the ZA84 alloy, especially after adding 0.3%Sc, the morphology of the Mg32(Al,Zn)49 phase in the alloy gradually changes from coarse continuous and/or quasi-continuous net to relatively fine quasi-continuous and/or disconnected shape, and the amount of the Mg32(Al,Zn)49 phase obviously decreases.
2) Adding 0.1%Sr, 0.5%Sn and 0.3%Sc to the ZA84 alloy can improve both the tensile strength and elongation of the alloy. Among the Sr-, Sn- and Sc-containing ZA84 alloys, the tensile properties of the Sr- and Sc-containing alloys at room temperature and 150 ?C are relatively high. In addition, adding 0.1%Sr to the ZA84 alloy is not beneficial to the creep properties, and adding 0.5%Sn to the ZA84 alloy has no obvious influence on the creep properties. However, adding 0.3%Sc to the ZA84 alloy can greatly improve the creep properties.
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(Edited by FANG Jing-hua)
Foundation item: Project(50725413) supported by the National Natural Science Foundation in China, Project(2007CB613704) supported by the National Basic Research Program of China, Project(2006AA4012-9-6) supported by the Chongqing Science and Technology Commission, China; Project(KJ090628) supported by the Chongqing Education Commission, China
Corresponding author: YANG Ming-bo; Tel: +86-23-68667455; E-mail: yangmingbo@cqut.edu.cn
