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Metals 2013, 3(4), 337-342; doi:10.3390/met3040337
Abstract: Chill casting of magnesium alloy samples with secondary alloying elements of Cu, Ca and Sn at % w.t. concentrations in the range 1–5, 0.1–5 and 0.1–3 respectively, gave rise to appreciably enhanced resistance to high-temperature creep, while maintaining good heat conductivity. The latter was considered to be driven by Cu and Mg-Cu intermetallics while it was clear that Sn mediated the high-temperature performance, mainly via networks of Mg2Sn and MgCaSn precipitates along the Mg matrix grain boundaries. It was postulated that Sn formed intermetallics by preferential substitution of Ca atoms and, thus, did not degrade the heat conductivity by retaining Cu. The % w.t. stoichiometry with the optimum combination of heat conductivity and resistance to high-temperature creep was found to be Mg-3Cu-1Ca-0.1Sn.
Spanning the spectrum of aeronautics and the space sector, to the more down to earth automobile industry [1,2] and the engineering/construction sector, magnesium and its light alloys are in direct competition with Al-based alloys and their associated light-element solubility-extension techniques [3,4,5,6,7,8] and underpin any structural choice that calls for low density and fair heat dissipation [1,2]. Lately, magnesium has also become a symbol of sustainable economic development, drawing attention as an element of preference towards the reduction of greenhouse gas emissions . Along with their advantages, two major drawbacks are also associated with magnesium alloys: (a) their problematic formability at ambient conditions, due to localized slip and stresses building up along grain boundaries upon mechanical deformation , and (b) their invariable failure in high-temperature applications . A typical example of the latter is the ASTM AZ91D magnesium alloy with a heat conductivity of approximately 73 W/mK ; when used in high temperature components heat dissipation is frequently inefficient, resulting in the component’s thermal deformation. Correspondingly, part of the ongoing research is related to Mg alloy stoichiometries that will maximize the material’s performance at high temperatures. As a first step, the addition of Ca, in replacement of the costly rare earth metals , is known to increase Mg alloy ductility through grain size reﬁnement in quantities of up to 0.3% . Ca also improves creep resistance, attributed to the thermal stability and the interface coherency between the Mg2Ca precipitates and the Mg matrix . The resulting Mg-Ca alloys show lower secondary creep rates and higher tensile strength than, e.g., the AZ91 alloy; these Mg-Ca alloy benefits are also coupled with improved castability and good melt handling [10,13]. Combined with secondary inclusions of Cu, the Mg-Ca system is a good example of alloy property tuning, outperforming the heat dissipation of the AZ91D alloy, largely due to its Cu content; however this improvement in high temperature performance comes at the price of reduced alloy corrosion, owing to precipitation of Mg2Ca intermetallics [9,15].
It could be argued that further alloying element modifications might benefit Mg alloy creep resistance at high temperatures, while preserving enhancements of heat conductivity. Tin has been known as such an alloying element, forming Mg-Sn intermetallic networks by mainly assuming Ca sites by substitution; these networks have been reported to block grain-boundary sliding, particularly at high temperatures . Hence, in the current work, the case is made for a Mg-Cu-Ca-Sn stoichiometry in which Sn substitutes Ca preferentially, while the alloy maintains a functional level of heat conductivity promoted by Cu; the proposed alloy is intended for high-temperature mechanical deformation and the synthesis route is proposed to be either gravity, pressure, or indeed chill casting, in a variety of moulds. Most importantly, however, no particular restrictions are set to the synthesis route’s solidification rate, as Mg-Sn networks have shown to form even at ambient cooling conditions.
2. Materials and Methods
Magnesium alloy samples were prepared by direct chill casting in five different runs that produced test samples of varying stoichiometries, in furnace ambient conditions. The elemental concentrations used varied in the ranges 1% w.t.–5% w.t. for Cu, 0.1% w.t.–5% w.t. for Ca and 0.1% w.t.–3% w.t. for Sn. In every run, an iron crucible was preheated to 500 °C in an electric furnace and its inner surface was coated by a chloride flux. The desired quantities of pure (~99.998%) Mg, Cu, Ca and Sn elements were then deposited in the crucible and brought to 750 °C. The melt was then stirred every half an hour for two hours and was left to rest for another four hours before being poured into a metallic mould with dimensions 30 × 30 × 200 mm. The ingots were then left to solidify at ambient conditions. The heat conductivities of the as-cast samples as well as of AZ91D alloy samples were determined by a transient laser flash method . Alloy creep resistance was examined via stress relaxation tests; for each sample, the stress decrease in respect with time was recorded up to a predetermined deformation, for an initial applied load of 100 MPa, while each sample was kept at 200 °C in atmospheric pressure. The applied load was then reduced gradually so as to keep the rate of displacement constant for each sample. X-ray diffraction (XRD) spectra were recorded on a Bruker D8-Focus diffractometer with nickel-filtered Cu Kα radiation (λ = 1.5405 Å), 40 kV and 40 mA. Sample cross sections were examined by scanning electron microscopy (SEM) on a Jeol 6380LV SEM.
3. Results and Discussion
Of the samples cast, only alloying compositions of 3% w.t. in Cu and 1% w.t. in Ca were found to be of engineering interest, yielding improved heat conductivity and creep resistance compared to the AZ91D reference alloy; hence only these stoichiometries will be the focus of the forthcoming discussion. For the remainder of the samples, generic comments will be made here. As indexed by energy-dispersive X-ray spectroscopy (EDS), alloy Cu concentrations in the order of 1% w.t. resulted in the precipitation of the CuMg2 intermetallic, mostly along grain boundaries. The concentration of these intermetallics was found to decrease with decreasing Cu content. Also, for Ca content roughly exceeding 5% w.t., a reduction in the material’s tensile strength and elongation prior to fracture was observed. The correlation between alloy mechanical properties and the alloying element content farther away from the apparent optimal 3% w.t in Cu and 1% w.t. in Ca was unclear and could not be drawn.
The chemical compositions of samples with engineering interest are listed in Table 1. In Sample S1 networks of the low-strength intermetallic CuMg2  and high-strength high-temperature Mg2Ca  phases (as indexed by XRD) were observed along grain boundaries. Addition of Sn in increasing amounts was observed to mediate formation of finer (and seemingly more continuous) intermetallic CuMg2 and Mg2Ca phases, as revealed by a comparison of Samples S2 and S3 with S1. Additionally, formation of the MgCaSn phase was also indexed in Samples S2 and S3. In the case of Sn-rich Samples, S4 and S5, the presence of the MgCaSn networks was again confirmed, albeit formed incompletely and appearing even within grains; particular to Sample S5, the low-melting-point Mg2Sn compound was also indexed as present.
|Sample index||Composition (% w.t.)||Heat conductivity (W/mK)||Load decrease (MPa)|
Heat conductivity and load decrease magnitude measurements are presented in Figure 1. As an introductory comment, the heat conductivity of reference Sample S1 (void of Sn additions) was appreciably high, at a value of 150 W/mK. All of Samples S2 through to S5 exhibited superior (higher) heat conductivities in comparison to that of the commercial AZ91D alloy as well as compared to S1. Altogether, Sn addition to Samples S2 to S4 was not found to cause appreciable differences to their heat conductivity (again, as compared to reference Sample S1). However, in the case of Sn-rich Sample S5, a marked reduction in heat conductivity was observed but the sample still dissipated heat more effectively than the AZ91D alloy. The latter observation could, potentially, flag an Sn composition maximum for enhanced conductivity behavior.
The stress decrease rate, shown in Figure 2, reached a plateau at the value for Sample S3; hence the 1% w.t. Sn content appears to offer optimal mechanical resistance to creep out of the stoichiometries tested in this work. This improvement in creep resistance may be explained by the existence of networks of CuMg2 intermetallics that form along grain boundaries ; in contrast, metallographic observations from the S1 sample revealed less frequent occurrences of this phase, however these observations were purely qualitative. In the case of Samples S2 through to S4, the stress decrease rate was more acute in the initial 3 h-period of the test, while during the remainder of the experiment this rate was essentially negligible. Sample S5 exhibited the lowest creep resistance, attributed to the alloy’s Sn content of 4% w.t., the precipitate networks of which were observed to include the Mg2Sn intermetallic.
For Sn concentrations higher than 0.1% w.t., the MgCaSn phase  was observed to precipitate along grain boundaries, in conjunction with the CuMg2 phase, forming intermetallic networks. For higher Sn content (the precise limit was unresolved but certainly higher than 2% w.t.), precipitation of MgCaSn intermetallics was observed within the grains and it was considered that they contributed less to localized slip control which, in turn, caused a reduction in creep resistance. Sn compositions as high as 3% w.t. caused the a joint precipitate of the low melting-point Mg2Sn intermetallic in addition to the MgCaSn phase, causing an even further reduction n of the material’s creep resistance. To generalize, precipitation of Sn-rich intermetallics was largely found to be a consequence of the competitive contributions by Sn and Ca; for Sn/Ca ratios below 3, formation of low melting-point intermetallics was generally suppressed, while for Sn/Ca ratios below 2, intermetallic networks were formed that improved high-temperature strength and creep resistance. Sn additions did not measurably affect the increased heat conductivity mediated by CuMg2 intermetallics, an observation that is probably underpinned by the thermodynamic preference of Sn to substitute Ca rather than Mg or Cu elements . Along these lines, an appropriate concentration for Sn in the Mg-3%Cu-1%Ca system appears to be in the range 0.1% w.t.–2% w.t.
Based on selected chill-cast Mg alloys, secondary inclusions of Ca and Sn formed intermetallics that precipitated in networks along grain boundaries and appeared to suppress grain-boundary slip at 200 °C. Furthermore, Cu elemental additions responsible for the alloy’s good heat dissipation were not affected, as Sn was observed to mainly interact with Ca and Mg.
Conflicts of Interest
The author declares no conflict of interest.
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