Process for producing TiB.sub.2 -dispersed TiAl-based composite material

Abstract

A TiAl intermetallic compound source and a boride which is less stable than TiB.sub.2 are mixed and melted, followed by solidification to form a TiB.sub.2 -dispersed TiAl-based composite material in which the TiB.sub.2 is contained in an amount of 0.3 to 10% by volume. In this process, the dispersed TiB.sub.2 particles become very fine, so that the hardness as well as the elongation and bending strength of the TiAl material are improved by the finely dispersed TiB.sub.2 particles.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a process for producing a TiB.sub.2 -dispersed TiAl-based composite material. More specifically, TiB.sub.2 is uniformely dispersed in TiAl intermetallic compound-based matrix.

2. Description of the Related Art

The TiAl intermetallic compound is promising as a light-weight high temperature structural material since it has both metallic and ceramic properties, has a low density and has an excellent high temperature specific strength. The TiAl intermetallic compound is however limited in its applications since its hardness is low in comparison with normal metals and alloys.

To improve the hardness of the TiAl intermetallic compound, a TiAl-based composite material in which TiB.sub.2 is dispersed was developed. For example, JP-A-03-193842, published in August, 1991, discloses a process for producing such a composite material, said process compressing mixing and melting powders of Al matrix containing TiB.sub.2 dispersed therein, Al metal powders and Ti metal powders, followed by solidifying the same to form a TiAl intermetallic compound in which TiB.sub.2 particles are dispersed.

As TiB.sub.2 particles are dispersed in TiAl intermetallic compound, generally, the hardness of the TiAl intermetallic compound increases but the ductility thereof decreases. It is therefore necessary that TiB.sub.2 particles are finely dispersed in the TiAl intermetallic compound. When the composite material is deformed, the matrix is deformed with cracks being formed. If the TiB.sub.2 particles dispersed in the matrix are large, cracks are interrupted by the TiB.sub.2 particles and the matrix cannot be deformed and is split or broken. In contrast, if the TiB.sub.2 particles dispersed in the matrix are fine, cracks may develop through the gaps between the TiB.sub.2 particles and the matrix can be deformed. Accordingly, it is considered that reduction of ductility of the matrix can be suppressed by finely dispersing TiB.sub.2 particles in the matrix.

In the above mentioned process of producing a TiB.sub.2 -dispersed TiAl intermetallic compound-based composite material, however, it is difficult to finely disperse TiB.sub.2 in a TiAl intermetallic compound since TiB.sub.2 particles agglomerate with each other when the mixture of the TiB.sub.2 -dispersed Al powders, Al metallic powders and Ti metallic powders are melted.

The purpose of the present invention is to provide a process for producing a TiB.sub.2 -dispersed TiAl intermetallic compound-based composite material in which the dispersed TiB.sub.2 is fine so that the reduction of the ductility of the material is suppressed while the hardness of the material is increased.

SUMMARY OF THE INVENTION

To attain the above and other objects of the present invention, there is provided a process for producing a TiB.sub.2 -dispersed TiAl-based composite material, comprising the steps of forming a molten mixture of a TiAl intermetallic compound source and a boride which is less stable than TiB.sub.2, and cooling and solidifying said molten mixture to form a TiAl-based composite material in which TiB.sub.2 is dispersed in an amount of 0.3 to 10% by volume of the composite material.

The TiAl intermetallic compound source may be a TiAl intermetallic compound itself, a mixture of Ti and Al metal powders, or a mixture of the compound and the powder mixture. The composition of the source is preferably such that Al is contained in an amount of 31 to 37% by weight of the total of Ti and Al.

The boride should be less stable than TiB.sub.2. Since TiB.sub.2 is generally most stable among metal borides, most metal borides may be used in the present invention. Such borides include, for example, ZrB.sub.2, NbB.sub.2, TaB.sub.2, MoB.sub.2, CrB, WB, VB and HfB.

The particle size of the boride to be mixed is not particularly limited but preferably less than 100 .mu.m, more preferably 30 to 0.1 .mu.m. If the particle size of the boride is larger than 30 .mu.m, the time for decomposing the boride is elonged. If it is smaller than 0.1 .mu.m, evaporation occurs during the melting step which reduces the yield.

The amount of the boride to be mixed is such that the obtained composite material will contain TiB.sub.2 in an amount of 0.3 to 10% by volume, preferably 1 to 5% by volume, based on the composite material.

If the content of TiB.sub.2 is less than 0.3% by volume, the hardness of the composite material is insufficient. If the content of TiB.sub.2 is larger than 10% by volume, the ductility of the composite material is significantly lowered.

In the process for producing a TiB.sub.2 -dispersed TiAl intermetallic compound-based composite material of the present invention, a molten mixture of the TiAl intermetallic compound source and the boride is first formed. This molten mixture is typically formed by heating a powder mixture of the TiAl intermetallic compound source and the boride to a temperature of about 1550.degree. to 1750.degree. C. If the temperature is lower than 1550.degree. C., it is difficult to obtain a uniform dispersion of TiB.sub.2. If the temperature is higher than 1750.degree. C., the yield of Al is lowered. Alternatively, it is possible that the TiAl intermetallic compound source be first heated to form a molten TiAl intermetallic compound source, followed by adding the boron particles into the molten TiAl intermetallic compound source.

The molten mixture is then cooled to room temperature. During the cooling, the molten TiAl intermetallic compound source becomes a TiAl intermetallic compound and the added boron, which is less stable than TiB.sub.2, reacts with Ti of the molten TiAl intermetallic compound source to crystallize or deposite TiB.sub.2 in the TiAl intermetallic compound matrix.

It is considered that the boride is dissolved and diffused in the molten Ti-Al. Since TiB.sub.2 is the most stable boride in the presence of Ti, boron (B), which became very fine by dissolution and diffusion of the boride, reacts with Ti to crystallize or deposite TiB.sub.2. This reaction to form TiB.sub.2 occurs uniformly in the molten mass so that fine TiB.sub.2 is formed uniformly in the TiAl intermetallic compound.

The particle size of TiB.sub.2 in the composite material may be made to be not larger than 10 .mu.m, further not larger than 5 .mu.m.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 shows the microstructure of the TiB.sub.2 -dispersed TiAl-based composite material in Conventional Example 1 (.times.100);

FIG. 2 shows the TiB.sub.2 powders used to prepare the composite material of FIG. 1 (.times.100); and

FIG. 3 shows the microstructure of the TiB.sub.2 -dispersed TiAl-based composite material in Example 6 (.times.100).

Example 1

A mixture of a sponge Ti and an Al ingot in a weight ratio of Al/(Ti+Al) of 0.34 was mixed with ZrB.sub.2 powders with an average particle size of 3 .mu.m in an amount of 3% by volume based on the volume of the total Ti-Al. The thus obtained mixture was charged in a water-cooled copper crucible in an arc furnace and maintained in an argon atmosphere at a temperature between 1550.degree. C. and 1750.degree. C. for 10 minutes, followed by cooling in the crucible to produce a button ingot of a TiAl intermetallic compound matrix containing 2.52% by volume of TiB.sub.2 dispersed therein.

Examples 2 to 8

The procedures of Example 1 were repeated, but the average particle size and amount of the boride to be mixed with the sponge Ti/Al ingot mixture were varied as shown in Table 1. The button ingots of a TiAl intermetallic compound matrix containing TiB.sub.2 particles dispersed therein in an amount as shown in Table 1 were produced.

Comparative Example 1

The procedures of Example 1 were repeated but the mixture of a sponge Ti and an Al ingot in an Al/(Ti+Al) weight ratio of 0.34 was mixed with CrB powders with an average particle size of 30 .mu.m in an amount of 0.2% by volume based on the volume of Ti-Al, to thereby obtain a button ingot of a TiAl intermetallic compound matrix containing 0.15% by volume of TiB.sub.2 particles dispersed therein.

Comparative Example 2

The procedures of Comparative Example 1 were repeated but the CrB powders mixed with the Ti-Al was changed to 15% by volume.

Thus, a button ingot of a TiAl intermetallic compound matrix containing TiB.sub.2 particles in an amount of 11.4% by volume was obtained.

Conventional Example 1

The procedures of Example 1 were repeated but the boride was changed to TiB.sub.2 powders with an average particle size of 7 .mu.m.

Thus, a button ingot of a TiAl intermetallic compound matrix containing 2.5% by volume of TiB.sub.2 particles dispersed therein was obtained.

Conventional Example 2

A mixture of a sponge Ti and an Al ingot in a weight ratio of Al/(Al+Ti) of 0.34 was mixed with B powders and, in accordance with the procedures of Example 1, a button ingot of a TiAl intermetallic compound matrix containing 2.4% by volume of TiB.sub.2 particles dispersed therein was obtained.

Conventional Example 3

A sponge Ti and an Al ingot were mixed in a weight ratio of Al/(Ti+A) of 0.34 and charged in a water-cooled copper crucible in an arc furnace, in which the mixture was maintained in an argon atmosphere at a temperature of 1600.degree. to 1700.degree. C. for 10 minutes and then cooled in the crucible to obtain a button ingot of a TiAl intermetallic compound.

Evaluations

Test pieces were cut from the button ingots of Examples 1 to 8, Comparative Examples 1 and 2, and Conventional Examples 1 to 3 and subjected to a Vickers hardness test and a bending test. The obtained hardness, elongation and bending strength of the test pieces are shown in Table 1.

TiB.sub.2 was identified by X ray diffraction. The volume fraction of TiB.sub.2 was determined by image analysis of micro structure of the composite.

TABLE 1__________________________________________________________________________ Amount of TiB.sub.2 in Average particle TiAl-based Bending size of additive Amount of composite material Hardness Elongation strength Additive (.mu.m) additive (vol %) (HV) (%) (MPa)__________________________________________________________________________Example1 ZrB.sub.2 3 3 vol % 2.52 355 0.90 8802 NbB.sub.2 3 3 vol % 2.85 372 1.1 9503 TaB.sub.2 3 3 vol % 2.85 350 1.05 9654 MoB 7 3 vol % 1.83 370 1.3 9815 CrB 30 0.5 vol % 0.38 307 1.4 9276 CrB 30 3 vol % 2.28 347 1.35 9207 CrB 30 10 vol % 7.6 395 0.95 9888 CrB 30 13 vol % 9.8 415 0.70 890ComparativeExample1 CrB 30 0.2 vol % 0.15 280 1.40 9302 CrB 30 15 vol % 11.4 420 0.20 650ConventionalExample1 TiB.sub.2 7 3 vol % 2.5 351 0.55 7792 B 3 3 at % 2.4 355 0.45 7503 -- -- -- -- 269 1.42 938__________________________________________________________________________

When the test pieces of Conventional Examples 1 and 2 in which TiB.sub.2 particles were dispersed in a TiAl intermetallic compound matrix are compared with the test piece of Conventional Example 3 of a TiAl intermetallic compound, the test pieces of Conventional Examples 1 and 2 are superior in their hardness but inferior in their elongation and bending strength. It is considered that the above results are caused because the TiB.sub.2 particles dispersed in the composite material are not fine. To confirm this, the microstructures of the test pieces of Conventional Example 1 and 2 were examined. FIG. 1 shows the microstructure of the test piece of Conventional Example 1 taken by microscope at a magnitude of 100. FIG. 2 shows the microstructure of the TiB.sub.2 powders used for preparing the test piece of Conventional Example 1 at a magnitude of 100. From these microstructures, it becomes apparent that the particle size of the TiB.sub.2 particles in the composite material in Conventional Example 1 increased from the 7 .mu.m particle size of the original TiB.sub.2 particles as mixed. A similar particle size increase was also found in the TiB.sub.2 particles in Conventional Example 2. The reason for the increase of the TiB.sub.2 particle size is thought because agglomeration of the TiB.sub.2 particles.

The TiB.sub.2 -dispersed TiAl-based composite materials of Examples 1 to 8, i.e., produced in accordance with the process of the present invention, had improved elongation and bending strength in comparison with the test pieces of Conventional Examples 1 to 2, which are comparative to those of Conventional Example 3, and also had an excellent hardness. It is considered that the reason for the improved elongation and bending strength in Examples is because the particle size of the TiB.sub.2 particles is finer. In the present invention, it is thought that the boride is dissolved and diffused in the molten Ti-Al, the free boron released from the decomposed boride reacts with Ti in the molten Ti-Al to form TiB.sub.2, which is the most stable boride in the presence of Ti, and thus crystallizes or deposits fine TiB.sub.2.

The microstructure of the test pieces of the Examples was examined. FIG. 3 shows the microstructure of the test piece of Example 6 taken by a microscope at a magnitude of 100. It is seen that the particle size of the TiB.sub.2 particles ranges from the submicrons size to a few micro meters, that is, very fine. In other Examples, the particles sizes of the TiB.sub.2 particles were found to be in the ranges from submicrons to a few micro meters.

It is thought that the elements other than B, such as Zr, Nb, Ta, Mo and Co, constituting the boride, are solid solved in the TiAl intermetallic compound and contribute to the improvement of the extension and hardness of the TiAl composite materials.

It is seen from Comparative Example 1 that if the content of the dispersed TiB.sub.2 in the composite material is less than 0.3% by volume, an improved hardness i.e., a desired effect of dispersing the TiB.sub.2 particles cannot be obtained. It is seen from Comparative Example 2 that if the content of the TiB.sub.2 particles is more than 10% by volume, the hardness of the composite material is improved but the elongation and bending strength of the composite material are significantly decreased. The reason for the significant decrease of the elongation and bending strength of the composite material is thought to be because of portion of the boride particles cannot be dissolved and remain as large particles.

Accordingly, it is seen that the TiB.sub.2 content of the TiB.sub.2 -dispersed TiAl-based composite material of the instant invention should be in a range of 0.3 to 10% by volume.

Claims

1. A process for producing a TiB.sub.2 -dispersed TiAl-based composite material, comprising the steps of:

forming a molten mixture of a TiAl intermetallic compound source and at least one boride which is less stable than TiB.sub.2 selected from the group consisting of ZrB.sub.2, NbB.sub.2, MoB.sub.2, CrB, WB, VB and HfB, and

cooling and solidifying said molten mixture to form a TiAl-based composite material in which TiB.sub.2 is dispersed in an amount of 0.3 to 10% by volume of the composite material.

2. A process according to claim 1, wherein said boride has an average particle size of 100 to 0.1 .mu.m.

3. A process according to claim 1, wherein said TiAl intermetallic compound source is a mixture of Ti and Al metal particles, the Al metal particles being in an amount of 31 to 37% by weight of the total of the Ti and Al metal particles.

4. A process according to claim 1, wherein said TiAl intermetallic compound source includes a TiAl intermetallic compound.

5. A process according to claim 1, wherein said boride is added in such an amount that the obtained TiAl-based composite material contains 1 to 5% by volume of the dispersed TiB.sub.2.

6. A process according to claim 1, wherein said molten mixture is heated up to a temperature of 1550.degree. C. to 1750.degree. C.

7. A process according to claim 1, wherein said TiB.sub.2 dispersed in said TiAl-based composite material has a particle size of less than 10 .mu.m.