High temperature oxidation of Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C alloy
Introduction
The two phase (γ-TiAl+α2-Ti3Al) alloys based on Ti-(45–48%)Al are attracting considerable attention from the aerospace and automobile industries, because of their low density, high melting point, and high specific strength. Of major concern are however their poor ductility at room temperature, their low strength, and insufficient oxidation resistance at high temperatures. Much effort has been directed toward improving these shortcomings by alloy modifications. The addition of Nb significantly increased the oxidation resistance of TiAl-based alloys by suppressing the TiO2-rich scale growth and increasing the scale adherence [1]. Tungsten also increased the oxidation resistance, and reduced the oxygen solubility or diffusivity in TiAl-based alloys [2], [3]. Silicon further increased the oxidation resistance as dissolved ions in the oxide scale [4] or by forming SiO2 islands at the scale/alloy interface [3]. Chromium however decreased the oxidation resistance by increasing the TiO2-rich scale growth [3], unless added by a quantity of more than 10% [5]. The compositions in this study are in atomic percentages, unless otherwise stated. Recently, we developed a new TiAl alloy, of which the composition was Ti–44Al–6Nb–2Cr–0.3Si–0.1C [6]. This alloy exhibited superior tensile strength at room temperature and 900 °C, and good oxidation resistance at 900 °C compared to the commercially available Ti–47.21Al–6.28Nb–0.49Cr–0.28Si–0.15Ni–0.17V alloy. In this study, another new TiAl alloy with a composition of Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C was developed. This new TiAl alloy displayed better oxidation resistance than our previous alloy [6] and other TiAl-X alloys (here, X = Si, refractory metals (viz. Mo, W, Ta), noble metals (viz. Pt, Au), transition metals (viz. Ni, Fe, Co, Mn, V), reactive metals (viz. Y, Zr, Hf), Nb-(Mn, Y, Ta, Zr, Hf, B), Nb–Cr–(W, Cu, Si, Mo), and Cr–(Si, Zr, Y, W, Ta)) [7]. The design concept of Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C was as follows: (i) control the amount of Al to have the duplex structure consisting of γ-grains and lamellar colonies of alternating layers of γ and α2 platelets for superior fracture toughness and creep resistance [8]; (ii) prepare a high Nb-containing alloy for good oxidation resistance [9], [10], high creep resistance, and good ductility at room temperature [11]; (iii) add W for oxidation resistance [2], [3], [9]; (iv) add Cr to improve ductility [6]; (v) add Si to improve high-temperature oxidation resistance [9] and mechanical properties [12]; and (vi) add C to improve high-temperature mechanical properties [12]. The aim of this study is to describe the oxidation characteristics of our new alloy at 700–1000 °C. The high-temperature oxidation kinetics obtained from short- and long-time isothermal and cyclic oxidation tests as well as the scale microstructure of the Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C alloy were discussed.
Section snippets
Experimental
The alloy with the composition of Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C was cast, and hot isostatic pressed at 1250 °C and 200 MPa in the Ar atmosphere for 2 h to eliminate pores. The prepared alloy was cut into rectangular samples (10 × 10 × 3 mm3), ground to a 1000 grit SiC finish, ultrasonically cleaned in acetone and methanol, and oxidized in atmospheric air. The short-time isothermal oxidation tests were performed at 900 and 1000 °C for 100 h using a thermogravimetric analyzer (TGA, Shimadzu
Results and discussion
Fig. 1 shows SEM microstructure of the prepared Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C alloy. Most of the areas consisted of α2/γ lamellae, which formed during casting. Locally, equiaxed areas that consisted of α2, γ, and β-Ti phases existed owing to hot isostatic pressing after casting.
Fig. 2 shows the weight gain versus oxidation time curves and the corresponding parabolic plots of Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C alloy. The weight gains were small, implying that protective oxide scales had
Conclusions
Based on the isothermal and cyclic oxidation tests conducted for Ti–46Al–6Nb–0.5W–0.5Cr–0.3Si–0.1C alloy, the following observations were made. When the alloy oxidized isothermally or cyclically at 900 and 1000 °C for 100 h, the outer rutile-TiO2 layer, the intermediate α-Al2O3 layer, and the inner (rutile-TiO2, α-Al2O3)-mixed layer formed. W, Cr, and Si tended to accumulate below the outer TiO2 layer due to their thermodynamic nobility compared to Ti and Al. The oxide scale began to spall
Acknowledgment
This work was supported by the Human Resource Development Program (No. 20134030200360) of the Korea Institute of Energy Technology Evaluation and Planning (KETEP) grant funded by the Korea government Ministry of Trade, Industry and Energy.
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