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Journal of Nanomaterials
Volume 2012 (2012), Article ID 708240, 6 pages
Direct Preparation of Nano-Quasicrystals via a Water-Cooled Wedge-Shaped Copper Mould
School of Materials Science and Engineering, Hebei University of Technology, Tianjin 300130, China
Received 30 June 2011; Accepted 9 August 2011
Academic Editor: Bo Zou
Copyright © 2012 Zhifeng Wang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
We have successfully synthesized multicomponent Mg-based nano-quasicrystals (nano-QCs) through a simple route by using a water-cooled wedge-shaped copper mould. Nanoscale QCs are prepared directly on tip of wedge-shaped castings. The further study shows that nano-QCs in the Mg71Zn26Y2Cu1 alloy show well microhardness of greater than HV450. Electrochemical properties of three kinds of quasicrystal alloys are investigated in simulated seawater. The Mg71Zn26Y2Cu1 nano-QC alloy presents the best corrosion resistance in this study for the formation of well-distributed nano-QC phases (1~5 nm) and polygonal Mg2(Cu,Y) nanophases (40~50 nm).
Quasicrystals (QCs) are aperiodic solids whose atomic arrangements have symmetries (typically five- or tenfold) that are forbidden for conventional crystallography  and have long been thought forbidden in nature. It brings about a paradigm shift in solid-state physics when the first QC example is obtained in a rapidly solidified Al-Mn alloy . The unexpected discovery of QCs presents scientists with a new, puzzling class of materials and involves hundreds of researchers in this realm. In the past nearly thirty years, QCs in various systems have been synthesized in laboratories [3, 4] and have also been discovered in natural minerals . These QCs possess a host of unusual mechanical and physical properties . Though they cannot be applied directly as structural materials for their innate brittleness, they present high microhardness which makes them used as good strengthening phases for some flexible matrix. Accordingly, diverse QC master alloys have been successfully synthesized and added into different commercial alloys [7, 8].
Usually, nano-quasicrystals (nano-QCs) can be synthesized through two kinds of ways. Nano-QCs are known to form in annealed [9, 10] or ball-milled  metallic glasses. Moreover, they can also be fabricated in extruded [12, 13], rolled , or wrought  Mg-based alloys at high temperature. These nano-QC alloys exhibit better mechanical properties compared with their corresponding glasses or conventional crystalline alloys . So, the nano-QC alloy is a kind of very promising material. In this study, we have synthesized nano-QC alloys through a new and simple route instead of traditional heat treatment and texturing process. Thus, the forming process of nano-QC alloy can strongly be simplified. At the same time, the costing of manufacture equipment can highly be cut down.
On the other hand, magnesium alloys present poor corrosion resistance. They can easily be eroded either in acid, neutral, or alkali solutions, even in pure water . So, their further applications are restrained. Considering the excellent corrosion resistance of QCs , we manage to in situ synthesis Mg-based nano-QCs in Mg-Zn-Y alloys which are hopeful to show their improved corrosion resistance.
In past work, we have synthesized quarternary spherical Mg-Zn-Y-based QC phase  by controlling compositions and undercooling conditions of the melts. In order to fabricate nanoscale QCs, we improve the cooling condition in this paper by using a water-cooled wedge-shaped copper mould . Multicomponent spherical nano-QCs are successfully synthesized and their electrochemical properties are investigated in simulated seawater.
The experimental alloys (Table 1) were produced by a reformed crucible electric resistance furnace (SG2-5-10 A, China), melted under the mixture of CO2/0.5vol.%SF6 protective atmosphere, using Mg(99.95%) and Zn(99.90%) ingots, Ni(99.99%) and Cu(99.99%) powder, and Mg-29.05%Y master alloy. Stirring for 2 min by impellor at 1073 K and holding for 5 min above 1053 K, the melt was poured and cooled in a water-cooled wedge-shaped copper mould. Samples were taken on tip of castings as shown in Figure 1.
The morphology observation of QCs was conducted using transmission electron microscopy (TEM, DEOL JEM-2010FEF, Japan). Microhardness of QC alloys was examined by microhardness tester (HXD-1000, China). The electrochemical properties of specimens were tested in simulated seawater (2.73% NaCl, 0.24% MgCl2, 0.34% MgSO4, 0.11% CaCl2, 0.08% KCl, and 96.5% deionized water, vol.%) by an electrochemical workstation (Gamry, PCI4-750, USA) with a sweep rate of 10 mV/s. A saturated calomel electrode (SCE) was used for the reference electrode.
3. Results and Discussion
TEM photos of QC alloys in different sample positions are shown in Figure 2. Three kinds of componential micro-/nano-QC phases are synthesized on tip of wedge-shaped castings. Energy-dispersive spectroscopy (EDS) analysis (Figure 3) shows that micro-/nano-QC phases in Position B of Alloy 1~ Alloy 3 are Mg-Zn-Y phase, Mg-Zn-Y-Cu phase, and Mg-Zn-Y-Cu-Ni phase, respectively. The selected area electron-diffraction (SAED) patterns with typical fivefold rotational symmetry identify that these micro-/nano-QC phases are icosahedral QCs. Among all QCs, QCs in Position A of Alloy 1 show petal-like morphology, while others show spherical morphology. From the further analysis in Table 2, we can see that in alloys with same components, QCs in Position B are smaller than those in Position A, while QC microhardness in Position B is greater than that in Position A. After introducing Cu(-Ni) into Mg-Zn-Y alloys, we can see in the same sample position, QC size of Alloy 2 and Alloy 3 is obviously smaller than that of Alloy 1. QC size of Alloy 2 in Position A is close to that of Alloy 1 in Position B. Nano-QC spheres about 8~30 nm and 1~5 nm are synthesized in Position B of Alloy 3 and Alloy 2, respectively. It shows from the microhardness testing that the smaller the QC spheres, the greater their value of microhardness. Furthermore, the microhardness of nano-QC spheres in Position B of Alloy 2 exceeds HV450, which shows fascinating properties.
Figure 4 shows the potentiodynamic polarization curves of QC alloys (Position B) measured in simulated seawater open to air at room temperature. We can see that Mg71Zn26Y2Cu1 nano-QC alloy presents high corrosion resistance in simulated seawater and its corrosion resistance is much better than that of Mg72Zn26Y2 and Mg71Zn26Y2Cu0.5Ni0.5 QC alloys. The further study shows that this result can be ascribed to the existence of well-distributed nano-QC phases (shown in Figure 5 by red arrows) and polygonal Mg2(Cu,Y) phases . These high-corrosion resistance phases decrease the anodic passive current density, improve the polarization resistance, cut down the corrosion rate (Table 3), and finally improve the corrosion resistance of the Mg-Zn-Y-based alloy markedly. Cu and Ni have long been considered as harmful elements for improving corrosion resistance of Mg-based alloy , however they are used to synthesize nano-QC spheres in this paper. Due to high-corrosion resistance of QC phases, Mg71Zn26Y2Cu1 and Mg71Zn26Y2Cu0.5Ni0.5 nano-QC alloys present better corrosion resistance than Mg72Zn26Y2 QC alloy. Moreover, the corrosion resistance of Mg71Zn26Y2Cu1 nano-QC alloys is higher than Mg71Zn26Y2Cu0.5Ni0.5 nano-QC alloys for the higher damage level of Ni to the corrosion resistance of magnesium alloy than that of Cu when they have same contents .
It was reported that a large negative enthalpy of mixing and/or existence of Frank-Kasper-type phases appear to be the crucial criteria for the formation of nano-quasicrystalline phase in any system . Meanwhile, Mg-Zn-Y-based QCs just belong to Frank-Kasper-type phases  and have a certain negative enthalpy of mixing. So theoretically, Mg-Zn-Y-based nano-QCs can be formed in a proper cooling conditions. The past cooling rate the researchers made to produce QCs was whether too high or too low, and was not content with the forming conditions of nano-QCs. This route just meets the demands for forming nanoscale QCs. So, nano-QCs are successfully produced in this paper. Moreover, the additions of Cu and Ni improve the degree of constitutional supercooling of Mg-Zn-Y melts and reduce the crucial criteria radius for forming spherical QCs. However, increasing thermodynamics undercooling coming from water-cooled wedge-shaped copper mould makes it still possible to form spherical QCs. At the same time, the alloy components designed for this study is based on the three empirical rules  for the formation of metallic glass. It has been widely accepted that quasicrystals and at least some metallic glasses are built up with icosahedral clusters . The short-range atomic configuration is very similar between the quasicrystal and amorphous phases . On the tip of the wedge-shaped ingots, its cooling conditions is just suitable for these icosahedral clusters to be nucleation of QCs. And then, it leaves very short time for quasicrystal growth. So, it is nano-QCs that form in this route instead of metallic glasses.
After introducing Cu(-Ni) into Mg-Zn-Y alloys, spherical nano-quasicrystals (nano-QCs) are directly prepared on tip of wedged-shaped castings. Nano-QCs in the Mg71Zn26Y2Cu1 alloy show well microhardness of greater than HV450. At the same time, the Mg71Zn26Y2Cu1 nano-QC alloy presents high corrosion resistance in simulated seawater for the formation of well-distributed nano-QC phases (1~5 nm) and polygonal Mg2(Cu,Y) nanophases (40~50 nm).
The authors would like to thank the financial supports from both Natural Science Foundation of Hebei Province, China (no. E2010000057) and International Science & Technology Cooperation Program of China (no. 2010DFA51850). The technical assistance of TEM testing from Dr. H. T. Fan, China National Academy of Nanotechnology & Engineering is also acknowledged.
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