Titanium aluminide for precision casting and casting method using the same

Abstract: A titanium aluminide is composed of 31.5 to 33.5 weight % of Al, 1.5 to 2.3 weight % of Fe, 1.5 to 4.8 (2.1 to 3.7 exclusive) weight % of Nb, 0.07 to 0.12 weight % of B with remainder being Ti and inevitable impurities. The 1.5-2.0 weight % of Nb may be replaced with 0.5 to 2.0 weight % of V if severe oxidization resistance is not necessary. The titanium aluminide is melted and poured into a mold, and the melt is cooled in the mold naturally.

Description: The present invention relates to titanium aluminide which is used as a material for precision casting, and particularly to titanium aluminide used for turbine parts, automobile parts and the like. Titanium aluminide (an intermetallic compound known by a chemical formula of TiAl (this substance will be referred to as "TiAl" hereinafter)) is drawing attention as an advanced light weight and heat resisting material. This is because the high specific strength of TiAl at elevated temperature is better than those of the nickel-base heat-resisting alloys, and the heat resistance, oxidation resistance and hydrogen embrittlement resistance of TiAl are better than those of the titanium alloys. Since TiAl possesses these and other admirable properties, there are demands to make aircraft jet engine parts such as blades and vanes out of this material. On the other hand, however, TiAl has a low ductility at ambient temperature and a strong dependency on the strain rate even at high temperatures (even at 700 o C or more) where sufficient toughness develops. This makes the machining or processing difficult. Therefore, TiAl cannot be used as a practical material up to date. Solving these difficulties contributes a lot to next generation aircraft jet engines and the like and therefore researches are being conducted from crystal structural and physical metallurgical viewpoints. As a result of such researches, methods of improving the low ductility by strengthening the grain boundaries and causing the plastic deformation by deformation twinning have been proposed in, for example, Japanese Patent Application Nos. 61-41740, 1-255632, 1-287243 and 1-298127. In spite of these efforts, however, misrun and cracks occur during the casting operation when TiAl is used to produce thin and complicated castings such as shrouded turbine blades. Regarding the above, the present assignee proposed new TiAl, which is superior in castability, in Japanese Patent Application No. 4-88140, published March 23, 1992 (or U.S. Patent Application No. 737,959 or European Patent Application EP-A-0 469 525) and Figure 8 of the accompanying drawings shows this. This TiAl does not have coarse lamellar structure (Figure 10), but microstructure (Figure 8), i.e., dispersed whisker-like (actually, flake-type) Ti-B compounds (TiB, Ti 3 B 4 , TiB 2 ). It should be noted that the publication 4-88140 or Figure 8 of the accompanying drawings does not constitute the prior art. Since the coarse lamellar grains cause the crackings but TiAl of Figure 8 does not have such coarse lamellar grains, TiAl of Figure 8 has an excellent castability. However, further researches revealed that TiAl of Figure 8 has too much dispersoids of Ti-B compounds, and the Ti-B compounds will become starting points of fatigue failure thereby reducing the fatigue properties. TiAl is expected as a new light-weight heat-resisting material, but conventional TiAl is difficult to process and the yield of the casting made from conventional TiAl is low. An object of the present invention is to provide TiAl that has an improved castability and oxidization resistance but does not have the dispersed Ti-B compounds which reduce the fatigue properties. According to one aspect of the present invention, there is provided TiAl which comprises Al 31.5-33.5% in weight, Fe 1.5-2.3% in weight, Nb 1.5-2.1 and 3.7-4.8% in weight and B 0.07-0.12% in weight, with remainder being Ti and inevitable impurities. V 1.5-2.0% may be used instead of Nb if a strong oxidization resistance is not necessary for a product. According to another aspect of the present invention, there is provided a method of producing a casting using the above TiAl, which comprises the steps of melting the TiAl, pouring the molten TiAl into a mold and cooling it naturally. The weight percents of the respective elements of the TiAl are determined due to following reasons: If Al is less than 31.5%, particularly if an Al/Ti ratio is smaller than 0.49, the cold (or ambient temperature) ductility drops considerably, and if Al is greater than 33.5%, particularly if an Al/Ti is greater than 0.55, the fracture toughness drops at ambient temperature (Figure 2 of the accompanying drawing). In Figure 2, X (K1c) represents the fracture toughness and its dimension is MPa√m. Fe plays a very important role in the present invention. Adding Fe lowers the melting point of TiAl by about 30-40 o C without enlarging a solid-liquid coexisting range of TiAl very much. This insures a desired fluidity during the TiAl casting operation and results in sound or defect-free products. In particular, when a thin casting such as a turbine blade is produced by a precision casting process, the melting point being low means that the good fluidity is maintained in the mold during the casting operation and the generation of coarse lameller grains is prevented by presence of beta phase, which depends on Fe, even at a relatively high cooling speed, which results in fine cast structure. If Fe is added less than 1.5%, an appropriate fluidity of the melt is not insured, and if Fe is added more than 2.3%, the beta phase precipitation undesirably increases thereby deteriorating the cold ductility. Nb is known as a beta stabilizer (beta former), and helps form more annealing twins and deformation twins which improves the cold ductility. Further, I experimented which element(s) improves the oxidization resistance if added together with Fe and found that Nb is the most preferred element. If Nb is added less than 1.5% in weight, the cold ductility is not improved, and if Nb is added more than 4.8%, the combined effect of Nb with Fe produces too much beta phase, which lowers not only the cold ductility but the strength at high temperature. The intermediate range of 2.1-3.7% is excluded since this amount (or percentage) results in 310 Hv (Vickers hardness) or more of castings at as cast state, as shown in Figure 3 of the accompanying drawings. With this hardness, thin precision cast products such as turbine blades are liable to crack even in the mold and/or the machining (or processing) of castings is difficult. If B is added 0.18-0.35% (Japanese Patent Application No. 4-88140), the flake-like Ti-B compounds are dispersed and this becomes a cause or starting points of fatigue failure. In this invention, therefore, B is reduced to 0.07-0.12%. This range of B suppresses the precipitation of Ti-B compounds and insures an appropriate fluidity. If B is added less than 0.07%, a sufficient grain boundary strengthening effect cannot be expected and the microstructure becomes unstable. If B is added more than 0.12%, the dispersion of Ti-B compounds appears as mentioned above. It should be noted that if a severe oxidization resistance is not necessary, 1.5-2.0% V may be used instead of 1.5-2.0% Nb. An Al/Ti ratio of TiAl is preferably 0.49-0.55. Figure 1 schematically shows a casting (product) when TiAl of the present invention is used in the precision casting; Figure 2 is a graph showing mechanical properties of TiAl (doped by Fe, Nb, B) in the as-cast state; Figure 3 is a graph showing the hardness of TiAl (doped by Fe, Nb, B) in the as-cast state; Figure 4 is a photograph (X200) showing the micro structure of the casting made from TiAl of the present invention; Figure 5 is a photograph (X1000) showing the micro structure having beta phase (white portions) when Fe is added to TiAl; Figure 6 is a photograph (X1000) showing the micro structure having beta phase (white portions) when Fe is added to TiAl at a higher cooling rate; Figure 7 schematically shows a casting when TiAl of Japanese Patent Application No. 4-88140 is used in the precision casting; Figure 8 is a photograph (X400) showing the micro structure of TiAl of Figure 7; Figure 9 shows a casting when conventional TiAl whose castability is not improved is used in the precision casting; and Figure 10 is a graph (X400) showing coarse lameller structure of TiAl (Ti-34.5 wt% Al) whose castability is not improved. Now, preferred embodiments of the present invention will be described with the accompanying drawings. TiAl of an embodiment includes in weight percent 31.5-33.5% Al, 1.5-2.0% Fe, 1.5-4.8% (2.1-3.7% exclusive) Nb and 0.07-0.12% B, with the remainder being Ti and inevitable impurities. TiAl of alternative embodiment includes in weight percent 31.5-33.5% Al, 1.8-2.3% Fe, 1.5-2.0% V and 0.07-0.12% B, with the remainder being Ti and inevitable impurities. The melting point of the TiAl, which is used as a material for the precision casting, is about 1480 o C. This value is lower than that of Ti-34.5wt%Al (1520 o C) by 30-40 o C. This TiAl is melted at a temperature of 1500 o C or more, for example 1550 o C, and poured into a mold to make a shrouded turbine blade by means of a known casting technique. The mold temperature is heated up to about 400-600 o C. The melt is cooled in the mold naturally. The cooling rate is such that the cast TiAl temperature becomes about 800-1000 o C in about 20 mins. Since the melt is poured into the mold of about 400-600 o C, the melt is not solidified in a moment and an appropriate fluidity is maintained prior to the solidification. This makes the sound precision casting possible. Figure 1 shows a shrouded turbine blade 1 made from TiAl of the present invention. This illustration is an illustration made from a photograph of the turbine blade actually produced by an experiment. To compare the turbine blade 1 of the present invention with the turbine blades by other TiAl, prepared are a turbine blade 2 (Figure 7) using TiAl of Japanese Patent Application No. 4-88140 which is developed by the present inventor and owned by the present assignee and a turbine blade 3 (Figure 9) using TiAl whose castability is not improved. Like the turbine blade of Figure 1, the turbine blades of Figures 7 and 9 are illustrations made from photographs of actual turbine blades produced by experiments. Although the same casting technique is employed to produce the turbine blades in Figures 1, 7 and 9, the turbine blades 1 and 2 of Figures 1 and 7 have completely good shape respectively whereas the fluidity of TiAl of Figure 9 is not satisfactory and the turbine blade 3 of Figure 9 does not have an appropriate appearance. TiAl of the present invention is an improvement of TiAl of Japanese Patent Application No. 4-88140. Specifically, TiAl of the present invention was found during the experiments for making TiAl of Japanese Patent Application No. 4-88140 more practical. Al is added 31.5%-33.5% in weight to maintain the ductility at ambient temperature and the fracture toughness at ambient temperature at appropriate levels respectively without deteriorating the castability. This primarily owes to the addition of Fe. Specifically, the beta phase (white portions in the photograph) are precipitated around the gamma grains, as seen from the photograph of Figure 5, and the coarse lameller structures are not seen. If the cooling rate is relatively high, for example if the melt of about 1550 o C is cooled to about 800-1000 o C in about 20 minutes, fine and dispersed beta phase are precipitated. As understood from Figure 6, the dispersed beta phase prevents the growth of gamma grains and the growth of coarse lameller structure caused by the transformation of alpha gamma + alpha2 ( α → γ + α 2 ). As a result, a fine cast structure is obtained as shown in Figure 4. Accordingly, the toughness of TiAl in the as-cast state is improved and the crackings are prevented. B is added 0.07%-0.12% in weight to strengthen the grain boundaries, stabilize the microstructure and prevent the dispersion of flake-like Ti-B compounds which would deteriorate the fatigue properties. In order to improve the oxidization resistance, the combined effect of several elements and Fe is experimented, and it is found that a certain amount of Nb and Fe improves the oxidization resistance more than the improvement by only Mo or the combination of Nb and Cr. Here, it should be noted that if the oxidization resistance is not required severely, V may be used instead of 1.5-2.0% Nb. As described above, TiAl of the present invention has a superior fluidity as well as high strength and relatively high ductility in the as-cast state. Further, the casting made from TiAl of the present invention does not have cracks even if the casting has a thin and complicated configuration. This improves the yield of sound castings. Therefore, the processing of the casting becomes easier and the cost is reduced. The present invention provides TiAl which can be used in an actual industry. According to the present invention, as mentioned earlier, the fluidity of TiAl is improved, the dispersion of flake-like Ti-B compounds which deteriorate the fatigue properties is prevented and the oxidization resistance is improved.

Claims: A method of precision casting an article, characterized in that it comprises the steps of: (A) preparing a titanium aluminide including in weight 31.5-33.5% of Al, 1.5-2.3% of Fe, 1.5-4.8% (2.1-3.7 exclusive) of Nb and 0.07-0.12% of B with the remainder being Ti and inevitably impurities; (B) melting the titanium aluminide; (C) pouring the melt into the mold; and (D) cooling the melt in a mold naturally. A method of precision casting an article, characterized in that it comprises the steps of: (A) preparing a titanium aluminide including in weight 31.5-33.5% of Al, 1.5-2.3% of Fe, 1.5-2.0% of V and 0.07-0.12% of B with the remainder being Ti and inevitably impurities; (B) melting the titanium aluminide; (C) pouring the melt into the mold; and (D) cooling the melt in a mold naturally. The method of claim 1 or 2, characterized in that the step (B) includes heating the titanium aluminide to 1500 o C or more and the step (D) is carried out such that the melt temperature is lowered to about 800-1000 o C in about 20 minutes. The method of claim 1, 2 or 3, characterized in that the method further includes the step of preheating the mold at about 400-600 o C prior to the step (C). The method of claim 1, 2, 3 or 4, characterized in that the step (D) is carried out such that beta phase is precipitated around a gamma particle and coarse lameller particles are not produced. The method of claim 1, 2, 3, 4 or 5, characterized in that the mold is a mold for casting a thin and complex shape product. A titanium aluminide for precision casting, characterized in that the titanium aluminide comprises in weight: 31.5-33.5% of Al; 1.5-2.3% of Fe; 1.5-4.8% (2.1-3.7 exclusive) of Nb; and 0.07-0.12% of B, with the remainder being Ti and inevitably impurities. A titanium aluminide for precision casting, characterized in that the titanium aluminide comprises in weight: 31.5-33.5% of Al; 1.5-2.3% of Fe; 1.5-2.0% of V; and 0.07-0.12% of B, with the remainder being Ti and inevitably impurities. The titanium aluminide of claim 7 or 8, characterized in that an Al/Ti ratio is 0.49-0.55.

Inventors: MATSUDA KENJI, MATSUDA, KENJI
Applicants: ISHIKAWAJIMA HARIMA HEAVY IND, ISHIKAWAJIMA-HARIMA HEAVY INDUSTRIES CO., LTD.
Application year: 1993
Main classification: C22C14
IPC codes: C22C14