JPH07197145A - Production of titanium aluminum base intermetallic compound sintered body - Google Patents

Abstract

PURPOSE:To provide a method to inexpensively produce a sintered body of a Ti-Al base intermetallic compound which is dense and excellent in ductility and toughness. CONSTITUTION:A powdery mixture is made by mixing a starting powder consisting of a powder containing titanium powder. TiAl3 powder and at least >=1 kind among VA or VIA group elements. This powdery mixture is formed in a prescribed shape to obtain a compact, and the compact is heated under zero pressure to synthesize the intermetallic compound consisting essentially of TiAl phase or/and Ti3Al phase and is sintered to obtain the sintered body. In this way, the Ti-Al base intermetallic compound sintered body easy to densify and excellent in strength is produced.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a Ti--Al based intermetallic compound sintered body, and more specifically, a Ti--Al based sintered body which is easily densified and has excellent strength, ductility and toughness. The present invention relates to a method for producing an intermetallic compound sintered body or a Ti-Al-based intermetallic compound-based composite sintered body.

[0002]

2. Description of the Related Art Precision casting and powder metallurgy are generally known as methods for producing Ti-Al based intermetallic compound parts. Among them, the precision casting method is a method in which the molten metal is prepared by arc melting, plasma melting, skull melting using high frequency as a heat source, or high frequency melting using a calcia crucible, and the above molten metal is cast into a mold manufactured by calcia or the like. is there. However, this precision casting method has problems that it requires a large amount of equipment and energy for melting and casting, and that the metallographic structure tends to become coarse.

On the other hand, the latter powder metallurgy method has recently attracted attention as an alternative manufacturing technique to the precision casting method because it can produce alloy parts having a fine structure and high ductility and toughness. The powder metallurgy method is classified into an alloy powder method and an elemental powder mixing method. The alloy powder method is a method of directly solidifying an alloy powder having a target composition by a HIP molding method or the like. On the other hand, the elementary powder mixing method is a method of manufacturing in the usual mixing, molding and sintering steps.

[0004]

However, in the alloy powder method, the powder is filled in a container having a hollow part having a desired part shape, and the HIP process is performed for each container. There is a problem in that a great amount of labor and cost are required for the container stripping work. Further, in the elementary powder mixing method, when a mixture of an aluminum powder having a low melting point and a titanium powder having a high melting point is sintered by an ordinary method, aluminum is melted in a temperature rising process, and a synthetic reaction between titanium and aluminum is caused. It is difficult to obtain a dense sintered body due to the generation of remarkable heat. For this reason, in the sintering step of the elementary powder mixing method, it is necessary to densify the sintered compact by gradually heating the powder compact while applying pressure in the HIP device to suppress the reaction rate. is there.

[0005] For example, as a method for producing a TiAl intermetallic compound material, a reactive sintering method using the reactive synthesis of Ti and Al (Japanese Patent Publication No. 1-30898) has been proposed. This is a method of obtaining a dense TiAl intermetallic compound material by solidifying and molding a mixed powder of Ti and Al, encapsulating it in an iron capsule or the like, and performing reaction synthesis by high temperature / high pressure treatment (HIP treatment). This manufacturing method requires high temperature and high pressure after encapsulating the solidified mixture (preformed product) in an iron capsule, etc., so it is necessary to remove the capsule, making it difficult to apply to parts with complicated shapes. Has the problem of being.

As described above, in all of these methods, H
There is a problem that IP processing is required and that it is difficult to form a complicated shape.

[0007] Therefore, the inventors of the present invention have earnestly studied to solve the problems of the prior art as described above, and as a result of various systematic experiments, the present invention has been accomplished.

(Object of the Invention) An object of the present invention is to provide a method for inexpensively producing a sintered compact of a Ti--Al based intermetallic compound which is dense and has excellent ductility and toughness. That is,
Manufacture of sintered parts or compacts of Ti-Al intermetallic compound that is dense and has excellent ductility and toughness by the usual powder metallurgical method of sintering in vacuum or an inert gas without using a HIP device. There is a way to do it.

The present inventors have focused on the following points with respect to the above-mentioned problems of the prior art. That is, first, Ti-
Focusing on the fact that the powder metallurgical method is most suitable as a method capable of inexpensively producing a sintered part of an Al-based intermetallic compound, and that the method requires further promotion of densification at the sintering temperature. did. Then, as a result of earnest researches focusing on promoting the densification at the sintering temperature, T
iAl phase (γ phase) or / and Ti ₃ Al phase (α
₍₂ phase) in the Ti-Al-based intermetallic compound as a main component, forming a new phase in equilibrium with the γ phase or α ₂ phase in the sintering temperature range, and having a very high mutual diffusion coefficient in the sintering temperature range. We focused on forming a new large phase. Then, by containing a 5A group or 6A group element as the raw material powder, it has been reached that a phase realizing the above and can be formed, and the present invention has been accomplished. From this, it is possible to solve the above-mentioned problems of the prior art and to inexpensively manufacture a component material having a fine structure and high ductility and toughness by a low-cost powder metallurgical method consisting of ordinary mixing, molding, and sintering. Came to.

[0010]

[Means for Solving the Problems]

(First Invention) A method for manufacturing a Ti—Al-based intermetallic compound sintered body according to the first invention comprises a titanium powder, a TiAl ₃ powder, and
A mixing step of mixing a raw material powder made of a powder containing at least one or more elements of Group A or Group 6A into a mixed powder; a molding step of molding the mixed powder into a predetermined shape to obtain a molded body; And a step of heating the body without applying pressure to synthesize and sintered an intermetallic compound having a TiAl phase and / or a Ti ₃ Al phase as a main component to obtain a sintered body.

(Second Invention) A method for producing a Ti—Al-based intermetallic compound-based composite sintered body according to the second invention comprises titanium powder and
A mixing step of mixing TiAl ₃ powder and at least one or more of boride powders mainly containing 5A group or 6A group to form a mixed powder, and molding the mixed powder into a predetermined shape to obtain a molded body. The TiA comprises a forming step and a sintering step in which the formed body is heated without pressure and sintered to form a sintered body.
It is characterized in that fine TiB ₂ particles are dispersed in an intermetallic compound matrix containing an l phase and / or a Ti ₃ Al phase as a main component.

[0012]

The mechanism by which the method for producing the Ti—Al-based intermetallic compound sintered body of the first invention and the method for producing the Ti—Al-based intermetallic compound-based composite sintered body of the second invention exert excellent effects is described. , It is not clear yet, but it is considered as follows.

(Operation of First Invention) A method for producing an intermetallic compound sintered body according to the present invention comprises a titanium powder and a TiAl ₃ powder,
A mixing step of mixing a raw material powder made of a powder containing at least one or more elements of the 5A group or 6A group into a mixed powder; a molding step of molding the mixed powder into a predetermined shape to obtain a molded body; And a sintering step in which the body is heated without pressure and a TiAl-based and / or Ti ₃ Al-based intermetallic compound is mainly sintered to obtain a sintered body.

TiAl ₃ is an intermetallic compound having a D0 ₂₂ structure at a melting point of 1350 ° C. This intermetallic compound is
Since the activity is significantly lower than that of ordinary titanium alloys, it can be melted in an inexpensive crucible. In addition, the deformation mode of TiAl ₃ alloy is limited due to restrictions on the crystal structure,
It has extremely brittle properties. Therefore, a fine powder can be easily formed from the TiAl ₃ ingot obtained by melting by a normal crushing process.

On the other hand, as the titanium powder, a commercially available pure titanium powder can be used. However, this powder is rich in ductility and the individual particle shape is complicated. Therefore, a mixed powder of this and TiAl ₃ powder has a good moldability. Are better. Therefore, by molding under normal pressure, it is possible to obtain the strength of the molded body that can sufficiently withstand practical use.

Further, in the sintering step, unlike the mixture of titanium powder and aluminum powder, the liquid phase that causes the generation of pores is hardly generated. Further, it has a feature that the heat of reaction between titanium and TiAl ₃ is significantly smaller than the heat of reaction between titanium and aluminum. Therefore, expensive pressure control or the like for suppressing the reaction in the sintering step is not necessary at all, and a dense part can be molded only by the normal pressureless sintering step.

Further, in the present method, since the 5A or 6A group element mixed in the raw material powder thermodynamically stabilizes the β phase, the TiAl phase (γ phase) and / or the Ti ₃ Al phase at the sintering temperature. Along with (α ₂ phase), β phase is in equilibrium. The mutual diffusion coefficient in this β phase is γ phase and / or
Alternatively, since it is remarkably large as compared with the α ₂ phase, diffusion of Ti, Al, 5A group (or 6A group) elements through this becomes orders of magnitude faster. Therefore, Group 5A or 6A in the raw material powder
The presence of powder containing at least one or more of the group elements,
The β phase is thermodynamically stabilized at the sintering temperature, and the presence of the β phase promotes the sintering, so that the densification in the sintering step is facilitated.

Further, in this method, the reaction proceeds in the solid phase state throughout, and the crystal grain size of the obtained sintered body exceeds the grain size of the raw material titanium powder as long as it is sintered under appropriate conditions. There is no. Therefore, it is possible to obtain a sintered body having a remarkably fine structure as compared with the product obtained by the usual melting method. Therefore, the obtained sintered body is characterized by extremely high strength, ductility and toughness.

As described above, according to the method for producing a Ti—Al-based intermetallic compound sintered body of the first invention, the TiAl ₃ -based powder is used as the aluminum source, and therefore, as when the aluminum powder is used. Since a liquid phase is not formed in the sintering process and the reaction heat is small, a normal sintering method that simplifies the control of the sintering conditions can be applied, and pressureless sintering becomes possible. Then, a Ti—Al-based intermetallic compound sintered body having a relative density of 98% or more can be easily obtained by adding the 5A group or 6A group element. Furthermore, since this method is a method based on a usual powder metallurgy method, the obtained sintered body has a fine crystal grain size and is excellent in strength, ductility and toughness. Moreover, it is possible to inexpensively manufacture a component material made of a sintered body of a Ti—Al-based intermetallic compound having a shape close to that of the final product.

(Operation of the Second Invention) Ti-Al of the Second Invention
In the method for producing a system-based intermetallic compound-based composite sintered body, titanium powder, TiAl ₃ powder, and at least one kind of boride powder mainly containing 5A group or 6A group elements are mixed and molded, and the molding is performed. The body is heated without pressure and sintered.

As described above, titanium powder, TiAl ₃ powder, and at least one kind of boride powder mainly containing a 5A group or 6A group element are mixed and molded, and the obtained molded body is not pressed. When fired at, the group 5A or group 6A element contained in the boride powder diffuses and forms a solid solution in the matrix. The 5A group or 6A group element promotes sintering due to the β-phase equilibrium and facilitates densification in the sintering step, as described in the operation of the first invention. Boron also reacts with titanium to form TiB ₂ particles. Sintering proceeds in parallel with such a metallurgical reaction, and finally a dense composite material in which TiB ₂ particles are uniformly dispersed in a Ti—Al-based intermetallic compound matrix is obtained.

By this sintering step, it is possible to obtain a dense composite sintered body in which TiB ₂ particles are uniformly dispersed in the Ti-Al intermetallic compound matrix. Further, the so-called pinning effect of TiB ₂ particles dispersed in the matrix suppresses the growth of crystal grains during sintering, so that the sintered body has a remarkably fine crystal grain size.
Therefore, in the main sintering step, a dense Ti—Al-based intermetallic compound-based composite sintered body having excellent strength, ductility, and toughness can be easily obtained.

In the method for producing a Ti—Al-based intermetallic compound-based composite sintered body according to the present invention, as described above, the sintering of the matrix is remarkably promoted by the 5A group or 6A group element in the boride powder. Since it is possible to exert the effect, it is possible to obtain a dense composite material having a substantially true density even when a large amount of the reinforcing phase is dispersed by simply firing without pressure. By this method, Ti-
It is possible to manufacture an Al-based intermetallic compound-based composite sintered body.

As described above, according to the method for producing a Ti—Al-based intermetallic compound-based composite sintered body of the second aspect of the present invention, since TiAl ₃ -based powder is used as the aluminum source, the aluminum powder is used in the sintering process. Since no liquid phase is formed and the reaction heat is small as in the case of using, the usual sintering method in which the control of the sintering conditions is simplified can be applied, and pressureless sintering becomes possible. Then, by adding the 5A group or 6A group element, a Ti—Al-based intermetallic compound group composite sintered body having a relative density of 98% or more can be easily obtained. Due to the extremely fine crystal grain size of the Ti-Al intermetallic compound matrix and the strengthening action of the uniformly dispersed TiB ₂ particles, the properties from room temperature to high temperature such as strength, rigidity and wear resistance were improved. A Ti-Al-based intermetallic compound-based composite sintered body can be obtained. Furthermore, since this method is a method based on the usual powder metallurgy method, Ti having a shape close to that of the final product is formed.
A component material made of a sintered body of an Al-based intermetallic compound can be manufactured at a lower cost.

[0025]

【The invention's effect】

(Effect of the first invention) By the manufacturing method of the first invention, it is possible to inexpensively obtain a dense sintered body of a Ti-Al-based intermetallic compound which is excellent in ductility and toughness.

(Effect of the Second Invention) According to the production method of the second invention, strength, rigidity, and strength of fine TiB ₂ particles dispersed in a Ti—Al-based intermetallic compound matrix having a fine crystal grain size are obtained. A Ti-Al-based intermetallic compound-based composite sintered body having excellent wear resistance can be obtained at low cost.

[0027]

EXAMPLES First, the method for producing the Ti—Al-based intermetallic compound sintered body of the first invention and the method for producing the Ti—Al-based intermetallic compound-based composite sintered body of the second invention will be described more specifically. The invention and the like (description of other inventions) will be described.

(Description of Other Inventions)

First, another invention of the method for producing a Ti—Al-based intermetallic compound sintered body of the first invention will be specifically described below.

The titanium powder used in the mixing step is generally called pure titanium powder and may be of any type. For example, (a) sponge fine, which is a by-product of sodium reduction sponge titanium,
(B) Hydrogenated and dehydrogenated titanium powder produced by hydrogenating → pulverizing → dehydrogenating magnesium reduction sponge titanium,
(C) Magnesium reduction method Three types of ultra-low chlorine titanium powder, which are produced by once dissolving titanium sponge titanium to remove impurities and then hydrogenating, crushing, and dehydrogenating, are typical. The titanium powder preferably has a maximum particle size of 50 μm or less. This is because the smaller the particle size of titanium powder is, the more excellent the sinterability is.
By setting it to be m or less, it becomes easier to manufacture a sintered body having a density of 98% or more by the method of the present invention only in the step of sintering. Here, a method of using titanium hydride powder instead of pure titanium powder is also conceivable, but titanium hydride powder is essentially difficult to reduce in oxygen in view of its manufacturing process, and plastic deformation Since it has almost no function, the moldability is extremely poor, and it is difficult to obtain a molded product strength that can be practically used. Therefore, it is not suitable as a raw material powder.

TiAl ₃ powder is the source of aluminum. By using the TiAl ₃ powder, the steps of mixing with titanium powder, molding, and sintering are generally facilitated.
A sintered body of an iAl-based and / or Ti ₃ Al-based intermetallic compound can be easily manufactured.

Here, TiAl series, TiAl ₃ series, Ti
₃ The “system” of Al-based is a general term for not only the composition ratio of Ti and Al, but also the composition ratio thereof, which is slightly deviated from the ratio, and / or a small amount of the third element. Since the TiAl ₃ -based alloy has a significantly lower activity than ordinary titanium alloys, it is possible to inexpensively produce an ingot having a low oxygen content by various melting methods. For example, a known method such as high-frequency melting using an ordinary crucible such as magnesia, plasma melting, or arc melting can be used. Further, since the TiAl ₃ alloy has a structure of D0 _{22 which} is essentially poor in ductility, it can be easily pulverized. That is, low oxygen powder can be manufactured at low cost by crushing the TiAl ₃ alloy ingot manufactured by the melting method with a smasher, an attritor, or the like. The TiAl ₃ powder is preferably finely divided into particles having an average particle size of 10 μm or less. If such a fine TiAl ₃ powder and a commercially available titanium powder of 50 μm or less are used, a compact sintered body having a relative density of 98% or more can be obtained only by molding and sintering according to the method of the present invention. Will be even easier.

The powder containing at least one element of Group 5A or Group 6A plays an important role in densifying the sintered body in the sintering step. That is, the 5
Group A elements (V, Nb, Ta) or 6A group elements (Cr, M)
o and W) have an important role of stabilizing the β phase and equilibrating the β phase together with the TiAl phase (γ phase) and / or the Ti ₃ Al phase (α ₂ phase) formed in the sintering process. As the powder containing the 5A group or 6A group element, a commercially available powder can be used as it is. The powder preferably has an average particle size of 10 μm or less. A powder having an average particle size of more than 10 μm is not preferable because the 5A group or 6A group elements are uniformly diffused and it takes a long time to stabilize the β phase. In addition, when the average particle diameter of the powder is 3 μm or less, further densification can be realized, which is optimal.

In this mixing step, titanium powder, TiAl ₃ powder, and powder containing at least one element of Group 5A or Group 6A are mixed so as to obtain a target composition ratio. The mixing method is not particularly limited, and a conventionally known powder metallurgy method can be applied, and a V-type mixer, a ball mill, a vibration mill or the like can be used. However, when the prepared powder containing the 5A group or 6A group element is a powder with remarkable agglomeration, if a high energy ball mill such as an attritor is used for a very short pulverization treatment,
This is preferable because the raw material powders can be uniformly mixed.

Here, the mixing ratio of the powder containing at least one element of the 5A group or 6A group is such that the volume ratio of the β phase equilibrating with the γ phase and the α ₂ phase at the sintering temperature is 30% by volume. It is preferable to set it as above. The appropriateness of this suitable blending ratio is Ti-Al-X (X: 5
It can be confirmed from the ternary phase diagram of group A or group 6A element). In this mixing step, it is possible to further add components other than the powders containing titanium powder, TiAl ₃ powder, which is the main component, and at least one or more elements of the 5A group or 6A group, and in this case, the fourth component Ingredient T
It may be added when the iAl ₃ powder is dissolved, or may be added as a powder when the pure titanium powder and the TiAl ₃ powder are mixed.

The molding step may be carried out by any molding method such as die molding, CIP molding, etc., in which the mixed powder is used as a component shape. The molding pressure is preferably 3 ton / cm ² or more. 3 ton /
It is not preferable to sinter a molded body that has been molded at a pressure of less than cm ² because it is difficult to improve the density of the obtained sintered body.

The sintering step is preferably carried out in vacuum or in an inert gas atmosphere. Sintering temperature is 1200 ° C
The range of 1400 ° C is preferred. If the temperature is lower than 1200 ° C, the formed intermetallic compound is not sufficiently homogenized, which is not preferable. Further, when the temperature exceeds 1400 ° C., the metal structure is likely to be coarsened, and a large amount of liquid phase may be generated during sintering, which may hinder the sintering. Is decreased, which is not preferable. The sintering time is preferably in the range of 1 to 24 hours. If the sintering time is less than 1 hour, the sintering will be insufficient and homogenization will not be possible, and if it exceeds 24 hours, the densification will not proceed further and it will be uneconomical in terms of energy. It is not preferable because the problem of dealumination occurs.

Among the raw material powders, TiAl _{3 as} an Al source
Has a melting point lower than that of titanium and around 1350 ° C., but higher than the melting point of aluminum which is 659 ° C. Therefore, 13
As long as the sintering is performed at 50 ° C or lower, no harmful liquid phase is generated during the sintering. Further, when titanium and aluminum react to form TiAl, heat generation of about 70 kcal / mol is involved, but the reaction heat when titanium and TiAl ₃ react to form TiAl is at most 20 kcal. As small as / mol. Therefore, a complicated simple device for controlling the synthesis reaction is not required, and the usual simple pressureless sintering process can be applied.

Further, β which is in thermodynamic equilibrium with the γ phase and the α ₂ phase during sintering by the 5A group or 6A group element
The phase has a crystal structure based on the bcc lattice, while the other two phases have a dense crystal structure based on the fcc and hcp lattices, respectively.
It is about 3 orders of magnitude larger than the γ and α ₂ phases. The sintering phenomenon that progresses due to the diffusion of these atoms is significantly promoted by the presence of 10% by volume or more of this β phase, and the densification of the sintered body in this step becomes extremely easy. It is more preferable that the volume ratio is 30% by volume or more. Further, this β phase significantly reduces the volume ratio upon cooling to room temperature after completion of sintering. The reason is that the lower the temperature,
This is because the volume fraction of the β phase that can equilibrate with the γ phase and the α ₂ phase decreases. As a result, the TiAl phase (γ phase) or /
And a Ti—Al-based intermetallic compound sintered body having a structure mainly composed of the Ti ₃ Al phase (α ₂ phase).

Further, if the densification is insufficient only by the sintering step, a true density component can be easily manufactured by performing HIP treatment after sintering. In this sintered body, the internal voids are completely isolated during the sintering process and do not communicate with the surface, so that the subsequent HIP treatment does not require can enclosure like the alloy powder method, and The HIP treatment can be performed as it is without coating the sintered body. Therefore,
Inexpensive processing is possible. The conditions for HIP processing are:
Considering reactivity with atmospheric gas, densification, economic efficiency, etc., using an inert gas such as argon or helium as a pressure medium, 1000 to 1400 ° C., 500 to 2000 atm,
It is preferable to carry out the treatment for 1 to 4 hours.

With such a simple process, it is possible to easily manufacture a sintered body of a Ti—Al-based intermetallic compound which is dense and has excellent ductility and toughness and has a product shape close to that of the product.

Next, a preferred method for producing a Ti—Al-based intermetallic compound sintered body according to the present invention comprises titanium powder, TiAl ₃ powder, and powder containing at least one element of 5A group or 6A group. A step of preparing a raw material powder (raw material powder preparing step), a step of pressurizing and rubbing at least titanium powder among the raw material powders to set a packing density of the raw material powder to a predetermined value (powder processing step), It includes a step of mixing raw material powders (a raw material powder mixing step), a step of molding the mixed powders (a molding step), and a step of firing the molded body without pressure (a sintering step).

Next, regarding the other invention of the method for producing the Ti—Al-based intermetallic compound-based composite sintered body of the second invention,
This will be specifically described.

Titanium powder and T used in the present invention
As the iAl ₃ powder, the same powder as described in detail in the above invention can be used. Further, any boride powder mainly composed of 5A group elements (V, Nb, Ta) and 6A group elements (Cr, Mo, W) can be used, and generally 1
A commercially available product in the form of fine powder adjusted to 0 μm or less can be used.

Detailed conditions and the like in the mixing step, the molding step and the sintering step in the present invention are the same as those in the steps described in the other inventions of the first invention. In the mixing step, the compounding ratio of the boride mainly composed of the 5A group or 6A group elements is such that the TiAl phase (γ phase) at the sintering temperature.
And / or the volume ratio of the β phase equilibrated with the Ti ₃ Al phase (α ₂ phase) is preferably 10% by volume or more.

As described above, the compounding ratio of the boride mainly composed of the 5A group or 6A group elements is Ti at the sintering temperature.
Since it is necessary to set the volume ratio of the β phase in equilibrium with the Al phase (γ phase) and the Ti ₃ Al phase (α ₂ phase) to a predetermined value, priority is given to the mixing ratio of the 5A group or 6A group elements. When added, the blending ratio of boron is uniquely determined.
When it is desired to control the proportion of boron independently, it is possible to add boron powder alone or in the form of titanium boride together with the boride.

The effect of TiAl ₃ powder at the time of sintering is
It is the same effect as the above-mentioned invention, and TiAl phase and Ti ₃
Does not require a complicated device for controlling the Al phase synthesis reaction,
Allows the application of normal pressureless sintering processes. Further, the 5A group or 6A group element in the boride diffuses and forms a solid solution in the matrix. As described in the above invention, the group 5A or group 6A element thermodynamically equilibrates the β phase with the TiAl phase (γ phase) and / or the Ti ₃ Al (α ₂ ) phase and sinters them. Significantly accelerates the process. At this time, the β phase is significantly promoted by the presence of 10% by volume or more,
The densification of the sintered body in this step becomes extremely easy. It is more preferable that the volume ratio is 30% by volume or more.

On the other hand, the boron in the boride is combined with titanium to form fine TiB ₂ particles and dispersed in the matrix. This is because the absolute value of the standard free energy of formation of each boride described above is generally smaller than that of titanium boride,
Moreover, it is not possible to thermodynamically equilibrate with the intermetallic compounds mainly composed of the TiAl phase or the TiAl ₃ phase except for TiB ₂ .

When the proportion of boron is manipulated independently, the amount of TiB ₂ produced by this reaction is preferably in the range of 3 to 30% by volume. When the amount of TiB ₂ is less than 3% by volume, the effect of refining and property improvement due to compounding of TiB ₂ particles is small, and when it exceeds 30% by volume, it becomes difficult to densify by sintering, and in addition, TiB 2 is added. _It is not preferable because the _two particles are likely to be unevenly dispersed.

Further, when the densification is not sufficient only by the sintering step, a true density component can be easily manufactured by subjecting to HIP treatment after sintering, as described in detail in the above invention. . Ti-A obtained by the production method of the present invention
The l-type intermetallic compound-based composite sintered body has a fine T-Al-based intermetallic compound matrix having a fine crystal grain size.
Since the iB ₂ particles are dispersed and compounded, the rigidity and the wear resistance are excellent in addition to the strength, the ductility, and the toughness.

A more preferred method for producing the Ti—Al-based intermetallic compound-based composite sintered body of the present invention is titanium powder and TiA.
l ₃ powder and at least one kind of boride powder mainly composed of 5A group or 6A group element are mixed and molded, and the molded body is heated without pressure, and β phase is present in an amount of 30% by volume or more. By sintering under conditions, a fine TiB ₂ content of 3 to 30% by volume in a TiAl-based and / or Ti ₃ Al-based intermetallic compound matrix is used.
This is to obtain a Ti—Al-based intermetallic compound-based composite sintered body in which particles are dispersed.

Another preferred method for producing a Ti—Al-based intermetallic compound-based composite sintered body of the present invention is titanium powder,
A step of preparing a raw material powder composed of TiAl ₃ powder and at least one kind of boride powder mainly containing a group 5A element or a group 6A element (raw material powder preparation step), and at least a titanium powder among the raw material powders A step of pressing and rubbing the raw material powder to a predetermined density of the raw material powder (powder processing step), a step of mixing the raw material powder (raw material powder mixing step), and a step of molding the mixed powder ( Molding step) and a step of heating the molded body without pressure to sinter it into a sintered body (sintering step).

These preferred production methods of the present invention are production methods characterized by the powder processing step. In this processing step, the titanium powder is pressed to some extent and the titanium powder is rubbed together to set the filling rate (filling density) of the titanium powder to a predetermined value. In this step, when the titanium powder is processed and rubbed together to be deformed, the projections of the individual particles of the titanium powder are crushed and the surface is smoothed. As a result, the fluidity of the powder is improved, the voids between the particles of the raw material powder are made fine, and the packing density is improved. When this powder is molded and sintered, the residual pores become extremely fine. Therefore, the fluidity of the powder is improved, and a desired packing density can be obtained.

In general, the packing density of a powder depends on the particle size distribution and the particle shape of the powder. That is, it is desirable that the particle size distribution be such that there is an appropriate amount of small and medium particles having the optimum particle size to fill the voids of the coarse particles, but even if the particle size distribution is optimum, if the fluidity of the powder is poor, the packing rate of the powder will be low. Does not improve. In the case of sponge fine (50 μm or less), the powder shape is porous and amorphous, and the fluidity is extremely poor, so the packing density (tap density) is 1.8 g.
It is about / cm ³ . In addition, the hydrogenated / dehydrogenated titanium powder has a square shape because it is a crushed powder, and although it is slightly superior to sponge fine, its fluidity is significantly inferior to ordinary atomized powder. It is about 2.2 g / cm ³ at most. Even if the raw material powder is molded in such a state, the particles hardly move due to the frictional force between the particles and are deformed as they are, so that coarse pores are easily formed in the molded body. further,
When this molded body is fired, coarse pores are inherited even in the sintered body, which easily becomes a starting point of fracture. Even if the molding pressure is increased to improve the density, it is difficult to make the residual pores in the sintered body fine. In order to improve the fluidity of these powders, the shape of the powders is changed by this processing step,
It is necessary to have the packing density of the above predetermined value.

In this processing step, 5% or more, more preferably 15% or more, when sponge fine is used as the titanium powder, based on the titanium powder currently on the market, hydrogenated / dehydrogenated titanium powder or extremely low chlorine. When titanium powder is used, it is preferable to deform the titanium powder by 10% or more so as to improve the packing density.

The packing density is 1.9 g / cm ^{3 to} 2.8.
It is preferably g / cm ³ . When the packing density is within this numerical range, it can have a proper fluidity and tap density. The packing density is 1.9 g / cm ^3.
If it is less than the above, coarse pores cannot be completely eliminated, so that the strength and ductility of the titanium-based composite material cannot be sufficiently improved, and if it exceeds 2.8 g / cm ^3. Both are not preferable because the moldability of the powder is significantly reduced.

When sponge fine is used as the titanium powder, the packing density of the powder is 2.0 g / cm ³ to.
As will be 2.4 g / cm ^3, In the case of using a hydrogenation-dehydrogenation titanium powder or an extremely low chlorine titanium powder, the packing density of the powder is between 2.3g / cm ³ ~2.7g / cm ³ It is preferable to add processing to each of the above. As a result, it is possible to eliminate coarse pores that can be the starting point of fracture.

The above-mentioned processing may be applied only to titanium powder, but at least titanium powder and TiAl ₃ powder, or titanium powder and TiAl ₃ powder and boride powder mainly containing 5A group or 6A group elements. Even when a mixture of one or more is mixed, it is excellent in strength, ductility, rigidity, wear resistance, and heat resistance, and is an extremely inexpensive Ti-Al-based intermetallic compound sintered body or Ti-Al-based intermetallic compound group. A composite sintered body can be obtained.

As a method of giving the above-mentioned processing, there are the following methods. That is, this step is a light processing such as smoothing the protrusions on the powder surface or crushing agglomerated powder such as sponge fine. For example, the raw material powder is placed in a ball mill or an attritor containing steel balls. It is carried out by, for example, a method of charging and stirring for a very short time (1 to 20 min.). By such a treatment, the titanium powder is rubbed against each other, and the projections thereof are pressed and flattened. As mentioned repeatedly, avoid crushing and refining titanium powder particles or subjecting them to strong processing that causes significant work hardening, since compressibility and formability will decrease, and the amount of oxygen will also increase. There must be.

As described above, the titanium powder is pressed and rubbed, and the packing density of the raw material powder is set to a predetermined value, so that the residual pores after molding and sintering can be made minute and isolated. Becomes

Therefore, according to the preferred manufacturing method of the present invention,
Even if an inexpensive titanium powder containing a large amount of impurities is used as a raw material, a TiAl-based material obtained by an extremely expensive melting method without sintering or HIP treatment, which causes a cost increase, or It is possible to obtain a Ti—Al-based intermetallic compound sintered body or a Ti—Al-based intermetallic compound-based composite sintered body that is superior in strength, ductility, rigidity, and wear resistance to TiAl-based composite materials. For this reason, the original cost merit of the sintered material can be fully exerted, and the Ti-Al-based intermetallic compound sintered body or the Ti-Al-based intermetallic compound-based composite sintered body can be used for mass-produced products such as automobile parts where cost is the highest priority. It will be possible to apply the body.

The mixing of the raw material powders in the raw material powder mixing step of the preferred production method of the present invention may be performed by any mixing method such as using a device such as a ball mill or a V-type mixer, but the boride particles are dispersed. It is preferable to use a high energy ball mill such as an attritor in order to make the temperature uniform. Further, in the molding step of this manufacturing method, as a method for molding the raw material powder subjected to the above-mentioned processing, there are methods such as die press molding and CIP (cold isostatic pressing) molding. Further, in the sintering step of this manufacturing method, the molded body is fired. The firing temperature and firing time are 1200 when considering the densification of the sintered body, the homogenization of the alloy composition, the dispersion state of TiB ₂ particles, the durability of the firing furnace, the economical efficiency, etc.
The temperature is preferably in the range of ~ 1400 ° C and 1-24 hours. Also,
The firing atmosphere is TiAl-based and / or Ti ₃
Since the intermetallic compound containing Al as a main component easily reacts with atmospheric gas (oxygen, nitrogen, hydrogen, and other reducing gases), in a high vacuum of 10 ⁻³ torr or less, or with argon,
It is preferable to use a high purity inert gas such as helium.

Examples of the present invention will be described below.

(First Example) -32 mesh TiAl
_{The 3} powders were inserted into an attritor together with steel balls and an agglomeration inhibitor, and pulverized for 60 minutes to obtain a fine powder having an average particle size of 4 μm. 371.8 g of the TiAl ₃ fine powder and -350 mesh pure titanium powder (sponge fine; Ti: 9
9.6%, O: 0.2%, Cl: 0.1%) 310.7 g
And molybdenum fine powder with a maximum particle size of 3 μm or less (purity: 9
9.5% or more) and 17.5 g were mixed in a ball mill for 30 minutes to obtain a mixed powder. Then, the mixed powder is mixed with C
Molding was performed with an IP device at a pressure of 4 ton / cm ² to obtain a cylindrical molded body. Then, the obtained molded body is subjected to 10 ^-5 Torr
In a vacuum of 1300 ° C. for 2 hours to sinter Ti-Al
A sintered intermetallic compound sintered body was obtained (Sample No. 1).

The obtained sintered body was subjected to structure observation and X-ray diffraction test. First, FIG. 1 shows an optical micrograph (magnification: 260 times) showing a metal structure of a cross section of the sintered body. Table 1 shows the phases identified by X-ray diffraction and the volume ratio of residual pores (porosity) measured from the cross-sectional structure of the sintered body.

[0066]

[Table 1]

As is clear from FIG. 1 and Table 1, the residual pores a of the sintered body obtained in this example are few,
It can be seen that the structure is a layered structure b composed of a TiAl phase (γ phase) + Ti ₃ Al phase (α ₂ phase) having a fine crystal grain size (average grain size: 50 μm).

(Second Embodiment) 336.5 g of TiAl ₃ fine powder produced in the same manner as in the first embodiment and pure titanium powder (sponge fine) 281.1 of -350 mesh.
g, and molybdenum fine powder (purity: 99.5% or more) 8
2.4 g was mixed, molded and sintered under the same conditions as in the first embodiment to obtain a TiAl-based intermetallic compound sintered body (sample number: 2).

Table 1 shows the X-ray diffraction results and the porosity measurement results of the obtained sintered body. As is clear from Table 1,
It can be seen that in the structure of the sintered body obtained in this example, the β phase is present at room temperature in addition to the γ phase + α ₂ phase. Further, it can be seen that the porosity is decreased and the densification is further advanced, compared with the sintered body obtained in the first example. That is, in this embodiment, a larger amount of molybdenum powder was mixed as compared with the first embodiment,
It was confirmed that the thermodynamic stability of the β phase increased as the β phase existed even at room temperature, and the volume ratio thereof remarkably increased at the sintering temperature, resulting in easier densification in the sintering process.

(Third Embodiment) 336.5 g of TiAl ₃ fine powder produced in the same manner as in the first embodiment and pure titanium powder of −350 mesh (hydrogenated / dehydrogenated titanium powder; T
i: 99.6%, O: 0.3%, Cl: 0.01%) 2
81.1 g and 82.4 g of fine molybdenum powder (purity: 99.5% or more) were mixed, molded and sintered under the same conditions as in the first embodiment to obtain a TiAl-based intermetallic compound sintered body. Obtained (sample number: 3).

An optical micrograph (magnification: 130 times) showing the metal structure of the cross section of the obtained sintered body is shown in FIG. 2, and the X-ray diffraction result and the porosity measurement result are shown in Table 1. As is clear from FIG. 2 and Table 1, the porosity is further reduced and the densification is further advanced as compared with the second embodiment. Further, it can be seen that the structure has the β phase c together with the layered structure b composed of the γ phase + α ₂ phase having a fine crystal grain size (average particle size: 60 μm). That is, it was confirmed that, in addition to the improvement of the thermodynamic stability of the β phase by molybdenum, the use of high-purity titanium powder facilitates densification in the sintering process.

(Fourth Embodiment) 336.5 g of TiAl ₃ fine powder prepared in the same manner as the first embodiment and pure titanium powder (sponge fine) 281.1 of −350 mesh.
g, and molybdenum fine powder (purity: 99.5% or more) 8
2.4 g was stirred and mixed in an attritor for 10 minutes and rubbed. Next, molding and sintering were performed under the same conditions as those in the first example to obtain a TiAl-based intermetallic compound sintered body (sample number: 4).

Table 1 shows the X-ray diffraction results and the porosity measurement results of the obtained sintered body. As is clear from Table 1,
The structure of the sintered body obtained in this example is composed of γ phase + α ₂ phase + β phase. Further, it can be seen that the porosity is further reduced and the densification is further advanced as compared with the sintered body obtained in the second example. That is, in this embodiment, the low-purity titanium powder having a high chlorine content is used by performing the rubbing treatment in the mixing step as compared with the second embodiment, but in the third embodiment. Similar to the case of using the high-purity titanium powder shown in FIG. 2,
It was confirmed that the densification in the sintering process was facilitated.

(Fifth Embodiment) 329.7 g of TiAl ₃ fine powder produced in the same manner as in the first embodiment, and pure titanium powder (hydrogenated / dehydrogenated titanium powder) 27 of −350 mesh 27
5.5 g and molybdenum boride (MoB) fine powder (purity:
99.5% or more, average particle size: 2 μm) and 94.8 g were mixed, molded, and sintered under the same conditions as in the fourth embodiment to obtain TiAl.
An intermetallic compound-based composite sintered body was obtained (Sample No. 5).

A scanning electron micrograph (magnification: 2000 times) showing the metallographic structure of the cross section of the obtained sintered body is shown in FIG.
Table 1 shows the line diffraction results and the porosity measurement results. As is clear from FIG. 3 and Table 1, almost no residual voids were observed, and it was found that fine TiB ₂ particles d were uniformly dispersed in the layered structure matrix b composed of the γ phase + α ₂ phase. Due to the pinning effect of the TiB ₂ particles, the TiAl phase + Ti ₃ A forming the matrix b
The crystal grain size of the l-phase is much finer than that of the third and fourth examples (average grain size: 8 μm).
Further, although it cannot be clearly discriminated from FIG. 3, a small amount of β phase is also observed in X-ray diffraction. That is, since the thermodynamic stability of the β phase is improved by the molybdenum boride, the densification in the sintering process is facilitated, and the fine TiB ₂ particles are dispersed / composited to have an extremely fine crystal grain size. It was confirmed that a TiAl-based intermetallic compound-based composite sintered body was obtained.

(Comparative Example 1) 235 g of pure Al powder of -350 mesh (purity: 99.8% or more) and pure titanium powder of -350 mesh (hydrogenated / dehydrogenated titanium powder; Ti: 9)
9.6%, O: 0.3%, Cl: 0.01%) 465 g
And were treated with a ball mill for 60 minutes to prepare a mixed powder. Next, using the obtained mixed powder, molding and sintering were carried out in the same manner as in the first embodiment, and a comparative sintered body of a TiAl-based intermetallic compound was obtained (sample number: C1).

An optical micrograph (magnification: 260 times) showing the metal-metal structure of the cross section of the obtained comparative sintered body is shown in FIG. Table 1 also shows the X-ray diffraction results and the porosity measurement results. As is clear from FIG. 4 and Table 1,
The structure of the comparative sintered body was composed of γ phase + α ₂ phase, but was extremely porous, and the porosity was 30% or more.

(Comparative Example 2) Sponge titanium block (Ti: 9)
9.6 g, O: 0.1%, Cl: 0.1%) 658 g and pure Al
Using 342g of lump (purity: 99.9% or more) as a raw material, high-frequency argon was melted in a calcia crucible and then cast into a mold to obtain T
A cast material for comparison of an iAl-based intermetallic compound was obtained (sample number: C2).

FIG. 5 shows an optical micrograph (magnification: 130 times) showing the metal-metal structure of the cross section of the obtained comparative sintered body. Table 1 also shows the X-ray diffraction results and the porosity measurement results. As is clear from FIG. 5 and Table 1,
Although the structure of the comparative sintered body is composed of γ phase + α ₂ phase, it can be seen that the structure is significantly coarser than the structures of the above-described examples according to the present invention shown in FIGS.

COMPARATIVE EXAMPLE 3 313.1 g of TiAl ₃ fine powder produced in the same manner as in the first example and 386.9 g of pure titanium powder (sponge fine) of −350 mesh were used in the first example. Mixing, molding, and sintering were performed under the same conditions as above to obtain a comparative sintered body of a TiAl-based intermetallic compound (sample number: C3).

An optical micrograph (magnification: 260 times) showing the metal-metal structure of the cross section of the obtained comparative sintered body is shown in FIG. Table 1 also shows the X-ray diffraction results and the porosity measurement results. As is clear from FIG. 6 and Table 1,
The structure of the comparative sintered body had a fine crystal grain size (average grain size:
It has a layered structure b composed of a γ phase + α ₂ phase having a diameter of 50 μm), but it can be seen that the residual pores a are slightly large.

[Brief description of drawings]

FIG. 1 TiAl obtained in the first embodiment of the present invention
It is an optical microscope photograph figure (magnification: 260 times) which shows the metal structure of the cross section of a system type intermetallic compound sintered compact.

FIG. 2 TiAl obtained in the third embodiment of the present invention
It is an optical microscope photograph figure (magnification: 260 times) which shows the metal structure of the cross section of a system type intermetallic compound sintered compact.

FIG. 3 TiAl obtained in the fifth embodiment of the present invention
FIG. 3 is a scanning electron micrograph (magnification: 2000 times) showing a metal structure of a cross section of a system-based intermetallic compound-based composite sintered body.

FIG. 4 is an optical micrograph (magnification: 260 times) showing a metal structure of a cross section of a comparative sintered body of a TiAl-based intermetallic compound obtained in Comparative Example 1.

5 is an optical micrograph (magnification: 130 times) showing a metal structure of a cross section of a comparative cast material of a TiAl-based intermetallic compound obtained in Comparative Example 2. FIG.

FIG. 6 is an optical micrograph (magnification: 260 times) showing a metal structure of a cross section of a comparative sintered body of a TiAl-based intermetallic compound obtained in Comparative Example 3.

[Explanation of symbols]

a ... residual pores b ... layered structure consisting of γ phase + α ₂ phase c ... β phase d ... TiB ₂ particles

Claims (7)

[Claims] 1. Titanium powder, TiAl ₃ powder and 5A
A mixing step of mixing a raw material powder consisting of a powder containing at least one or more of Group 6 or Group 6A elements into a mixed powder; a molding step of molding the mixed powder into a predetermined shape to obtain a molded body; a sintering step of the intermetallic compounds mainly heated TiAl phase or / and Ti ₃ Al phase and synthetic sintered to the sintered body by pressureless, characterized by comprising the Ti- A method for manufacturing an Al-based intermetallic compound sintered body. 2. The method for producing a Ti—Al-based intermetallic compound sintered body according to claim 1, wherein the mixed powder is pressed and rubbed before the molding step. 3. The Ti according to claim 1, wherein the sintering step is performed under the condition that the β phase is present in an amount of 10% by volume or more.
-A method for manufacturing an Al-based intermetallic compound sintered body. 4. Titanium powder, TiAl ₃ powder and 5A
A mixing step of mixing at least one boride powder mainly composed of Group 6 or Group 6A element to form a mixed powder; a molding step of molding the mixed powder into a predetermined shape to form a molded body; The body is heated without pressure and is sintered to form a sintered body. The TiAl phase and / or T
A fine TiB ₂ particle is dispersed in an intermetallic compound matrix containing an i ₃ Al phase as a main component.
A method for producing an i-Al-based intermetallic compound-based composite sintered body. 5. The method for producing a Ti—Al-based intermetallic compound-based composite sintered body according to claim 4, wherein the mixed powder is pressed and rubbed before the forming step. 6. The Ti according to claim 4, wherein the sintering step is performed under the condition that the β phase is present in an amount of 10% by volume or more.
—Method for producing Al-based intermetallic compound-based composite sintered body. 7. The mixing step further comprises boride powder or /
5. A method for producing a Ti—Al-based intermetallic compound-based composite sintered body according to claim 4, characterized by mixing titanium boride powder and titanium boride powder.