JPH03177524A - Manufacturing method of metal matrix composite material - Google Patents

Abstract

PURPOSE:To produce a superior composite material free from the occurrence of micropores by bringing a green compact consisting of the fine pieces of Al, the fine pieces of Ni and Cu, and the fine pieces of Ti having respectively prescribed volume percentages into contact with molten light alloy. CONSTITUTION:A mixture is prepared by mixing 60-80vol.% of fine pieces of Al (alloy), 1-10vol.% of fine pieces of Ni, Cu, or an alloy composed essentially of them or mixture thereof, and 1-10vol.% of fine pieces of Ti (alloy), and the above mixture is compacted so as to be formed into a green compact in which the total volume percentage is regulated to 62-95% is formed. This green compact is immersed into molten light metal selected from Al (alloy) and Mg (alloy) and to be a matrix metal, and the above molten metal is infiltrated without pressurization into the green compact. By this method, the length of time necessary to bring the green compact into contact with the molten metal can be shortened, and a metal matrix composite can be efficiently produced.

Description

DETAILED DESCRIPTION OF THE INVENTION Field of the Invention The present invention relates to a composite material, and more particularly to a method for manufacturing a metal matrix composite material using short fibers as a reinforcing material and an aluminum alloy as a matrix.

Conventional technology As a method for producing a metal matrix composite material, Japanese Patent Application No. 108165/1989 filed by the same applicant as the present applicant discloses a method of forming a molded body containing a reinforcing material and fine pieces of a specific metal. However, a method has already been proposed in which at least a portion of the molded body is brought into contact with a molten metal of the matrix metal, and the molten metal is allowed to permeate into the molded body without substantially applying pressure. According to the proposed method, the molten matrix metal penetrates into the compact along the fine pieces of the specific metal, and the heat generated by the reaction between the specific metal and the matrix metal improves the permeability and wetting of the reinforcing material. Since the properties of the composite material are improved and good composite formation is achieved, the composite material can be efficiently manufactured at a low location without pressurizing the molten matrix metal.

Problems to be Solved by the Invention However, in this method, depending on the manufacturing conditions of the composite material, the temperature of the molten metal of the matrix metal may be relatively low.
If the molded body is immersed in the molten metal for a relatively short period of time, micropores may occur in the composite material. For example, SiC particles with a volume fraction of 5% (average particle diameter 10μII), Al alloy powder (Al-12%Si, average particle diameter 40μm) with a volume fraction of 30%, pure Cu powder with a volume fraction of 30% (average particle diameter A molded body consisting of 30μ11) was heated to 575°C with an Al alloy (
A composite material was manufactured by immersing it in a molten metal of JIS standard AC8A) for 15 seconds, and its cross section was observed under an optical microscope. It was found that a small number of micropores were mainly caused by insufficient impregnation of the molten Al alloy. It was recognized that

In view of the above-mentioned problems in the method according to the above-mentioned earlier proposal, the present invention has been made by setting the temperature of the molten metal of the matrix metal to a relatively low value and setting the time during which the molded body is immersed in the molten metal to be relatively short. The object of the present invention is to provide a method that can produce a good composite material without producing micropores even if the material is mixed.

Means for Solving the Problems According to the present invention, the above-mentioned object is achieved by achieving a volume ratio of 60 to 80.
% of Al or Al alloy fine pieces, volume fraction of 1 to 10% of N 1 s Cu or an alloy whose main component is either of these, or a mixture thereof, and volume fraction of 1 to 10% of Ti. or fine pieces of Ti alloy, and the total volume fraction of these fine pieces is 62 to 95%.
A method for producing a metal matrix composite material, the method comprising: contacting a molten metal of a light metal selected from the group consisting of Mg5Mg alloys and infiltrating the molten metal into the molded body without substantially applying pressure; Al or Al with a ratio of 60 to 80%
Fine pieces of alloy, fine pieces of Ni SCu with a volume fraction of 1 to 10%, or a mixture thereof containing any of these as a main component, and fine pieces of Ti or a Ti alloy with a volume fraction of 1 to 10%. and the total volume fraction of these fine pieces and the reinforcing material is 62 to 95%, and the molded body is made of Al, Al alloy, Mg as a matrix metal.
This is achieved by a method for manufacturing a metal matrix composite material, in which the metal matrix composite material is brought into contact with a molten metal of a light metal selected from the group consisting of Mg alloys, and the molten metal is infiltrated into the molded body without substantially applying pressure.

Effect of the invention According to the present invention, fine pieces of Al or Al alloy, Ni, C
Fine pieces of u or an alloy having any of these as a main component or a mixture thereof, and fine pieces of Ti or a Ti alloy are used.

Fine pieces of Al or Al alloys have excellent compatibility with molten metals such as Al alloys, and the tendency of Nis Cu or alloys mainly composed of either of these to form oxides is relatively small, and the amount of surface oxide film is small. Therefore, these fine pieces have excellent wettability with molten metal such as Al alloy. When the compact is brought into contact with a molten matrix metal and heated by the heat of the molten metal, Al in the fine pieces of Al or Al alloy (and Al or Mg in the matrix metal) reacts well with Ni or Cu. While forming fine intermetallic compounds, a suitable amount of heat is generated, and the heat melts the fine pieces of Al or Al alloy and improves the wettability of the fine pieces and reinforcing material to the molten metal. The Al alloy penetrates well toward the center of the molded body, and the molten matrix metal penetrates better into the molded body from the periphery, and as a result, the matrix metal is composited with at least fine intermetallic compounds. A good composite material is formed that is reinforced and free of micropores.

Further, according to the present invention, by setting the volume fraction of fine pieces of Al or Al alloy to be relatively high at 60 to 80%,
The porosity of the molded body is set to be relatively low. Furthermore, when Ti, which has a high tendency to form nitrides and oxides, is heated by the heat generated by the combination reaction or the heat of the molten metal, it reacts with nitrogen and oxygen, which are the main components of the air present in the voids of the compact. Also, some of the oxygen in the air present in the voids of the molded body reacts with the molten Al, thereby substantially removing the air in the molded body, which also prevents the generation of micropores. Prevented.

Furthermore, according to the present invention, if the melting point (solidus temperature) of the light metal as the matrix metal is T''C, the temperature of the molten light metal is within the solid-liquid coexistence temperature range of T-T+50°C. However, in this case, the solid phase ratio of the molten metal is preferably 70% or less, particularly 50% or less.

The fine metal particles in the present invention may be in the form of powder, short fibers, whiskers, etc. In the case of powder, the average particle size is 1 to 500 μm, particularly 3 to 200 μm.
The average fiber diameter is preferably about α, and in the case of short fibers and whiskers, the average fiber diameter is 0. 1μ～1■, especially 1～200
μ-san, average fiber length 1μIm~1011ff11 especially 1~
It is preferable that the thickness be about 200μ.

Further, the reinforcing material in the present invention may be in the form of short fibers, whiskers, particles, etc., and the size of the reinforcing material is such that in the case of short fibers and whiskers, the average fiber diameter is 0.1 to 20 μm, particularly 0.3 μm. ~10μ top, average fiber length 5μ11-10III
11 It is particularly preferable that the amount is about 10 μml to 31,
In the case of particles, the average particle size ranges from 0°1 to 100μ, especially from 1 to 100μ.
The thickness is preferably about 30 μm.

The Ni content of the Ni alloy used in the present invention is 50
vt% or more, particularly 80wt% or more, excluding unavoidable impurities. Elements other than Ni may be any elements, but in particular Ag, Al s Bs Co S
Cr s Cu s F e , M g SM n
sMos Pbx S is Sn, Ta,”riSv
SZns2" is preferable.

Similarly, the Cu content of the Cu alloy used in the present invention is preferably 50vt% or more, particularly 80vt% or more, and the elements other than Cu may be any element after removing inevitable impurities. However, especially Ag1Al, B5Co, Fe
%Mg, Mn5Ni, Pb.

Preferred are Si, 5nSTa, Ti5VSZr, and Zn.

Further, the Ti content used in the present invention is preferably 50 wt% or more, particularly 80 vt% or more, and unavoidable impurities are removed (elements other than Ti may be any element, but in particular A ISV, Sn.

Preferably, they are Fe, Cu%MnSMo, Zr5Cr, and Si%B.

DESCRIPTION OF THE PREFERRED EMBODIMENTS The invention will be explained in detail below by way of example embodiments with reference to the accompanying figures.

Example 1 Alumina-silica short fibers (manufactured by Isolite Industries Co., Ltd.) with an average fiber diameter of 3 μm and an average fiber length of 1.5II11 and an Al alloy powder (JIS standard AC8A) with an average particle size of 150 μm
) or Al powder alloy powder with an average particle size of 100μ scratches (JIS
Standard AC7A) and pure Ti powder with an average particle size of 20μ,
By mixing pure Ni powder with an average particle size of 20 μm in various ratios and compression molding, the volume ratio can be reduced as shown in Figure 1, unless the total volume ratio exceeds 95%. 0%, 5%, 10%, 15%, 20% alumina-silica short fiber 10 and volume percentage 40%, 50%, 60%, 70
%, 80% Al alloy powder 12, volume percentage 0%, 1%,
5%, 10%, 15% pure Ti powder 14 and volume fraction 0%
, 1%, 3%, 5%, 7%, 10%, and 15% pure Ni powder 16, and a molded body 18 having dimensions of 45 x 25 x 10 aa+ was formed.

Then, as shown in FIG.
Each molded body 18 is sequentially immersed in a molten metal 22 of Al alloy (JIs standard AC8A) maintained at 70°C, and after maintaining this state for about 30 seconds, the molded body is taken out from the molten metal, and the molten metal is solidified in that state. I let it happen.

Next, the thus formed composite material was cut and the impregnated state of the molten metal was investigated by observing its cross section, and the results shown in Tables 1 and 2 below were obtained. In Tables 1 and 2, ◎ indicates that no micropores were present, O indicates that a very small amount of micropores were generated, and Δ indicates that a small amount of micropores were generated. It shows that In particular, Table 1 shows that the volume percentage of alumina-silica short fibers is 0%, 5%, 10%, 1
5%, 20% and the volume percentage of pure Ni powder is 0%, 15
%, and Table 2 shows the results when the volume percentage of alumina-silica short fibers is 0%, 5%, 10%, 15%, 2
0% and the volume percentage of pure Ni powder is 1%, 3%, 5%,
The results are shown for cases of 7% and 10%.

From Tables 1 and 2, regardless of the composition of Al alloy powder, Al
It can be seen that the volume fraction of the alloy powder is preferably 60 to 80%, and the volume fraction of both the pure Ni powder and the pure Ti powder is preferably 1 to 10%.

In addition, when the cross section of the composite material indicated by ◎ in Table 2 was investigated by X-ray diffraction, pure Ni powder almost completely reacted with Al to form intermetallic compounds NiAl3 and NiAl, and alumina - When the volume fraction of silica short fibers is 0%, the Al alloy as a matrix is compositely reinforced by these intermetallic compounds, and when the volume fraction of alumina-silica short fibers is 5 to 20%, It was recognized that the Al alloy as a matrix was compositely reinforced not only by alumina-silica short fibers but also by intermetallic compounds.

Example 2 SiC whiskers as a reinforcing material with a volume percentage of 5% (manufactured by Tokai Carbon Co., Ltd., average fiber diameter 0.3μ11 average fiber length 1
00 μa+), pure Al powder with a volume fraction of 70% (average particle size 50 μm), and pure Ni powder with a volume fraction of 5% (average particle size 30 μm).
μm) and pure Ti powder with a volume fraction of 5% (average particle size 30μ1
1) and compression molded to form four molded bodies.
Composite materials were prepared in the same manner and under the same conditions as in Example 1 above, except that molten Al alloy (JIS standard A2024) was used at temperatures of 600°C, 650°C, 700°C, and 750°C. The impregnated state of the molten metal was investigated by observing the cross section of the product.

As a result, it was found that a good composite material was formed without the formation of micropores, regardless of the temperature of the molten matrix metal.

Example 3 SiC particles (manufactured by Showa Denko K.K., average particle size 30μ11) as a reinforcing material with a volume fraction of 10% and A with a volume fraction of 60%
l Alloy powder (JIS standard A2024, average particle size 150μ
11) and pure Ni powder with a volume fraction of 8% (average particle size 30μ1)
1) and pure Ti powder with a volume fraction of 3% (average particle size 30μlI)
) is mixed and compression molded to form a molded body, and a molten Al alloy (Al-30% Cu) in a semi-molten state at a temperature of 550°C is used as the molten metal for the matrix metal. A composite material was formed in the same manner and under the same conditions as in Example 1 above, except that the immersion time of the molded body was set to about 30 seconds, and the impregnation state of the molten metal was determined by observing the cross section of the composite material. investigated.

As a result, it was confirmed that a good composite material containing no micropores was formed in this example as well.

When the cross-sections of the composite materials formed in Examples 2 and 3 were examined by X-ray diffraction, pure Ni powder almost completely reacted with Al to form intermetallic compounds N iA 13 , N
i A is 1, and A as Matri Sokusu
It was recognized that the l alloy was compositely strengthened not only by the reinforcing material but also by these intermetallic compounds.

Example 4 Alumina short fibers (IC1) with a volume fraction of 15% as a reinforcing material
"Saphir RF" manufactured by Aisin Seiki Co., Ltd., average fiber diameter 3 μ field, average fiber length 1 mm) and Al alloy fiber with a volume ratio of 65% (manufactured by Aisin Seiki Co., Ltd., Al-5% Mg, average fiber diameter 60 μ
■, average fiber length 31111), pure Ni fiber (manufactured by Tokyo Rope Co., Ltd., average fiber diameter 20 μ layer, average fiber length 11! m) with a volume percentage of 5%, pure Tim fiber (manufactured by Tokyo Rope Co., Ltd., average fiber length 11! m) with a volume percentage of 10%) Manufactured by Seizuna Co., Ltd., average fiber diameter 20 μm 1 average fiber length 111
11) were mixed and compression molded to form a molded body made of these.

Next, this molded body was placed in a mold (JIS Regulation No. 110) at 400°C, and an Mg alloy (S
A molten metal of AE standard AZ91) was poured, and sulfur hexafluoride gas was poured onto the surface of the molten metal to prevent oxidation of the Mg alloy, and then the molten metal was cooled to room temperature.

Next, the composite material thus formed was cut and the impregnated state of the molten metal was investigated by observing its cross section, and it was found that a good composite material containing no micropores was formed in this example as well. It was done.

Furthermore, when the cross section of the composite material formed in this example was investigated by X-ray diffraction, it was found that the matrix in the central part was Al.
alloy, the peripheral matrix is an Mg alloy,
Pure Ni fibers react with Al to form an intermetallic compound N i A
13, NiAl, especially in the periphery, pure Ni fibers also react with Mg to form an intermetallic compound Mg2.
It also becomes N iSMgN i2, and the ratio of these intermetallic compounds increases toward the outer periphery.
It was observed that the matrix was compositely reinforced not only by the reinforcing material but also by these intermetallic compounds.

In this example, a composite material was formed in the same manner by replacing the Ni fibers with the pure Ni powder used in Example 3, and the molten Mg alloy was replaced with the molten pure Mg at a temperature of 680°C. When a composite material was formed in the same manner by replacing it, a good composite material containing no micropores was able to be formed in each case.

Example 5 Pure A, 1 powder with a volume fraction of 72% (average particle size 50 μm),
A molded body made of pure Ni powder (average particle size 30μff1) with a volume fraction of 6% and pure Ti powder (average particle size 30μff1) with a volume fraction of 5% is mixed and compression molded, A composite material was formed in the same manner and under the same conditions as in Example 1 above, except that a molten Al alloy (JIS standard A2024) with a hot water temperature of 650° C. was used as the molten matrix metal.

Next, the state of impregnation with the molten metal was investigated by observing the cross section of the composite material thus formed, and it was found that a good composite material containing no micropores had been formed. In addition, when examining the cross section of the composite material by X-ray diffraction, it was found that the matrix in the center and the periphery was substantially pure Al and Al alloy, respectively, and the pure Ni powder almost completely reacted with Al to form an intermetallic compound. NiAl3, NiAl
It was recognized that the matrix was compositely reinforced by these intermetallic compounds.

In this example, the molten matrix metal was heated to a temperature of 6.
When a composite material was similarly formed by replacing the molten metal with pure Mg at 80° C., a good composite material containing no micropores could be formed in this case as well.

Example 6 A composite material was formed in the same manner and under the same conditions as in Example 1 above, except that pure Cu powder with an average particle size of 30 μm was used instead of pure Ni powder, and its cross section was observed. The impregnation state of the molten metal was investigated by doing this.

As a result, the same results as in Example 1 described above were obtained. That is, it was confirmed that regardless of the composition of the Al alloy powder, the volume fraction of the Al alloy powder is preferably 60 to 80%, and the volume fraction of both pure Cu powder and pure Ti powder is preferably 1 to 10%. .

In addition, when the cross section of the composite material formed by setting the volume fraction of Al alloy powder, pure Cu powder, and pure Ti powder to the above-mentioned preferred range was investigated by X-ray diffraction, it was found that pure C
U powder almost completely reacts with Al to form intermetallic compounds such as CuAl2, and when the volume fraction of alumina-silica short fibers is 0%, the Al alloy as a matrix is reacted with these intermetallic compounds. When the volume fraction of alumina-silica short fibers is 5 to 20%, the Al alloy as a matrix is compositely reinforced not only by alumina-silica short fibers but also by intermetallic compounds. Admitted.

Example 7 A composite material was manufactured in the same manner and under the same conditions as in Example 2 above, except that pure Cu powder with an average particle size of 30 μ4 was used instead of pure Ni powder.

As a result, it was found that a good composite material was formed without the formation of micropores, regardless of the temperature of the molten matrix metal.

Example 8 A composite material was manufactured in the same manner and under the same conditions as in Example 3 above, except that pure Cu powder with an average particle size of 30 μm was used instead of pure Ni powder.

As a result, it was confirmed that a good composite material containing no micropores was formed in this example as well.

In addition, when examining the cross section of the composite materials formed in Examples 7 and 8 by X-ray diffraction, it was found that the pure Cu powder almost completely reacted with At to become intermetallic compounds such as CuAl2. It was recognized that the Al alloy as a matrix was compositely strengthened not only by the reinforcing material but also by these intermetallic compounds.

Example 9 A composite material was produced in the same manner and under the same conditions as in Example 4 above, except that pure Cu fiber (Tokyo Rope Co., Ltd. % formula %) was used instead of pure Ni fiber, The state of impregnation of the molten metal was investigated by observing the cross section.

As a result, it was confirmed that a good composite material containing no micropores was formed in this example as well.

Furthermore, when the cross section of the composite material formed in this example was investigated by X-ray diffraction, it was found that the matrix in the central part was Al.
alloy, the peripheral matrix is Mg, and pure C
U fibers react with Al to form intermetallic compounds such as Cu A 12, and especially in the periphery, pure Cuff1 fibers become M
The ratio of these intermetallic compounds increases toward the outer periphery, and the matrix is not only reinforced by the reinforcing material but also by these intermetallic compounds. It was also observed that the steel was reinforced in a composite manner.

In this example, a composite material was formed in the same manner by replacing the Cu fibers with the pure Cu powder used in Example 8, and the molten Mg alloy was replaced with a molten Mg alloy at a temperature of 680°C. When a composite material was formed in the same manner by replacing it with , a good composite material containing no micropores was able to be formed in each case.

Example 10 A composite material was formed in the same manner and under the same conditions as in Example 5 above, except that pure Cu powder with an average particle size of 30 μm was used instead of pure Ni powder.

Next, the state of impregnation with the molten metal was investigated by observing the cross section of the composite material thus formed, and it was found that a good composite material containing no micropores was formed. In addition, when examining the cross section of the composite material using X-ray diffraction, it was found that the pure Cu powder almost completely reacted with Al, resulting in CuA.
It was found that the matrix was compositely reinforced by these intermetallic compounds.

In this example, the molten matrix metal was heated to a temperature of 6.
When a composite material was similarly formed by replacing the molten metal with pure Mg at 80° C., a good composite material containing no micropores could be formed in this case as well.

Example 11 Alumina-silica short fibers with an average fiber diameter of 3 μm and an average fiber length of 1.5 I1 m (manufactured by Isolite Industries Co., Ltd.) and Al alloy powder with an average particle size of 150 μm (JIS standard AC8A)
Or Al powder alloy powder (JIS standard AC7A) with an average particle size of 100 μm, pure Ti powder with an average particle size of 30 μm, pure Ni powder with an average particle size of 30 μm, and pure Cu powder with an average particle size of 30 μm. By mixing at various ratios and compression molding, alumina with a volume ratio of 0%, 5%, 10%, 15%, and 20% is produced, except when the total volume ratio exceeds 95%.
Silica short fibers and volume percentage 40%, 50%, 60%, 70
%, 80% Al alloy powder and volume fraction 0%, 1%, 5%
, 10%, 15% pure Ti powder, pure Cu powder with a volume fraction of 0.5%, and a volume fraction of 0°5% to 15% (every 0.5%)
of pure Ni powder and formed into a shaped rod having dimensions of 45×25×10+on.

In addition, the volume fraction of pure Ni powder was set to 0.5%, and pure Cu
A molded body having dimensions of 45 x 25 x 10 cm was formed in the same manner, except that the volume fraction of the powder was set at 0.5% to 15% (in 0.5% increments).

Next, a composite material was formed in the same manner and under the same conditions as in Example 1 above, except that the molded body thus formed was used, and the impregnation state of the molten metal was investigated by observing its cross section. .

As a result, as in the case of Example 1 above, regardless of the composition of the Al alloy powder, the volume fraction of the Al alloy powder is 60 to 80%, and the volume fraction of pure Ni powder + pure Cu powder is 1 to 10%. It was confirmed that the volume fraction of the pure Ti powder is also preferably 1 to 10%.

Also, Al alloy powder, pure Ni powder + pure Cu powder, and pure T
When the cross section of the composite material formed by setting the volume fraction of i powder to the above-mentioned preferred range was investigated by X-ray diffraction, it was found that pure Ni powder and pure Cu powder were almost completely Al
reacts with NiAl3 or NiAl and Cu, respectively.
When the volume fraction of alumina-silica short fibers is 0%, the Al alloy as a matrix is compositely strengthened by these intermetallic compounds, and the alumina-silica short fibers become intermetallic compounds such as A12. Fiber volume percentage is 5~
In the case of 20%, it was recognized that the Al alloy as a matrix was compositely reinforced not only by the alumina-silica short fibers but also by the intermetallic compound.

Example 12 Except that pure Ni powder (average particle size 5 μm) with a volume ratio of 2.5% and pure Cu powder (average particle size 30 μm) with a volume ratio of 2.5% were used instead of pure Ni powder. A composite material was manufactured in the same manner and under the same conditions as in Example 2 above.

As a result, it was found that a good composite material was formed without the formation of micropores, regardless of the temperature of the molten matrix metal.

Example 13 Instead of pure Ni powder, pure Ni powder (average particle diameter 10 μm) with a volume fraction of 3% and pure Cu powder (average particle diameter 20 μm) with a volume fraction of 3% were used.
A composite material was produced in the same manner and under the same conditions as in Example 3 above, except that μ11) was used.

As a result, it was confirmed that a good composite material containing no micropores was formed in this example as well.

When the cross sections of the composite materials formed in Examples 12 and 13 were examined by X-ray diffraction, pure Ni powder and pure Cu powder almost completely reacted with Al, resulting in NiA
It was found that the Al alloy as a matrix was compositely strengthened not only by the reinforcing material but also by these intermetallic compounds.

Example 14 Instead of pure Ni fibers, pure Ni fibers with a volume percentage of 5% (average fiber diameter increased by 30 μm, average fiber length 3 II m) and pure Cu fibers with a volume percentage of 5% (average fiber diameter 20 μm, average fiber length 1 aIl) were used.
A composite material was produced in the same manner and under the same conditions as in Example 4 above, except that 1) was used, and the impregnation state of the molten metal was investigated by observing its cross section.

As a result, it was confirmed that a good composite material containing no micropores was formed in this example as well.

In addition, the cross section of the composite material formed in this example is
When investigated by line diffraction, the central matrix was A
The matrix in the peripheral part is Mg, and the pure Ni fibers and pure Cu fibers react with Al to form intermetallic compounds NiAl3 and Cu A12, respectively. Especially in the peripheral part, pure Ni The fibers and pure Cu fibers also reacted with Mg to form intermetallic compounds such as NiMg2 and MgCu2, respectively, and it was recognized that the matrix was compositely strengthened not only by the reinforcing material but also by these intermetallic compounds. .

In this example, a composite material was formed in the same manner by replacing the Ni fibers and Cu fibers with the pure Ni powder and pure Cu powder used in Example 13, respectively, and the molten Mg alloy was When a composite material was similarly formed by replacing the molten metal with pure Mg at 680° C., a good composite material containing no micropores could be formed in both cases.

Example 15 Instead of pure Ni powder, pure Ni powder (average particle size 15 μa+) with a volume percentage of 4% and pure Cu powder (average particle size 2
A composite material was formed in the same manner and under the same conditions as in Example 3 above, except that 5 μm) was used.

Next, the state of impregnation with the molten metal was investigated by observing the cross section of the composite material thus formed, and it was found that a good composite material containing no micropores was formed. Furthermore, when the cross section of the composite material was examined by X-ray diffraction, pure Ni powder and pure Cu powder almost completely reacted with Al, and NiAl3. , CuAl2, and other intermetallic compounds, and it was recognized that the matrix was compositely strengthened not only by the reinforcing material but also by these intermetallic compounds.

Example 16 Instead of pure Ni powder, pure Ni powder (average particle size 15 μα) with a volume ratio of 5% and pure Cu powder (average particle size 25 μα) with a volume ratio of 5% were used.
A composite material was formed in the same manner and under the same conditions as in Example 5 above, except that μ11) was used.

Next, the state of impregnation with the molten metal was investigated by observing the cross section of the composite material thus formed, and it was found that a good composite material containing no micropores was formed. Furthermore, when the cross section of the composite material was investigated by X-ray diffraction, it was found that the matrix in the center and the periphery was substantially pure Al and Al alloy, respectively, and pure Ni powder and pure Cu
The powder almost completely reacts with Al to form NiAl3 and NiAl3, respectively.
It was observed that the matrix was compositely reinforced by these intermetallic compounds, such as Cu A 12.

In this example, the molten matrix metal was heated to a temperature of 6.
When a composite material was similarly formed by replacing the molten metal with pure Mg at 80° C., a good composite material containing no micropores was also formed in this case.

In this example, the molten matrix metal was heated to a temperature of 6.
When a composite material was similarly formed by replacing the molten metal with pure Mg at 80° C., a good composite material containing no micropores could be formed in this case as well.

Although fine particles having a specific composition are used in each of the above embodiments, the fine particles in the present invention may have any composition. For example, the composition of Al alloy is JIS
Standard AC7A% JIS standard ADC12, JIS standard AD
May be Ti7.8%Al-3.5%Mg etc., Ni
The composition of the alloy is, for example, N 1-50% Al, Ni-30%
Cu, Ni-39, 5% Cu-22, 1% Fe = 8.8
%B, etc., and the composition of the Cu alloy is, for example, Cu-5
0% Al, Cu-29.6% Ni-22, 1% Fe-8
, 8% B, etc. Particularly when the Ni alloy and Cu alloy are Ni-Cu alloys, the content ratio of Ni and Cu may be any ratio; It may be 1% B or the like.

Although the present invention has been described in detail with reference to a number of embodiments above, the present invention is not limited to these embodiments, and various other embodiments are possible within the scope of the present invention. This will be obvious to those skilled in the art. For example, part or whole of Ni or Ni alloy fine pieces or Cu or Cu alloy fine pieces may be Ag or Ag alloy fine pieces or A
It may be replaced with fine pieces of u or Au alloy.

Effects of the Invention As is clear from the above explanation, according to the present invention, the molten matrix metal penetrates well into the entire molded body, Ti reacts with nitrogen and oxygen in the molded body, and Ti reacts with nitrogen and oxygen in the molded body. Because part of the oxygen reacts with Al, the air in the compact is substantially removed, making it possible to produce an even better composite material free of micropores.

Further, according to the present invention, the molten metal of the matrix metal may be at a relatively low temperature, and the formed body may contain Ni or Ni.
In the case of the method according to the above-mentioned earlier proposal, the time for contacting the molded body with the molten metal can be shortened compared to the case where fine pieces of alloy, etc. or fine pieces of Ti or Ti alloy are not included. Composite materials can be manufactured using even more efficient equipment compared to conventional methods.

table table

[Brief explanation of drawings]

Figure 1 shows alumina-silica short fibers, Al alloy powder and pure T.
FIG. 2 is a perspective view showing a compact made of i powder and pure Ni powder, and FIG. 2 is an illustrative sectional view showing the compact shown in FIG. 1 immersed in a molten Al alloy. 10...Alumina-silica short fiber, 12...Al alloy powder, 14...Pure Ti powder, 16...Pure Ni powder. 18... Molded body, 20... Heater, 22... Al
Patent for molten alloy Patent: Toyota Motor Corporation
Patent attorney Masa Akashi
Tsuyoshi figure

Claims (2)

[Claims] (1) Fine pieces of Al or Al alloy with a volume ratio of 60 to 80%, fine pieces of Ni, Cu, or an alloy containing any of these as the main component, or a mixture thereof, with a volume ratio of 1 to 10%, containing fine particles of Ti or Ti alloy at a rate of 1 to 10%,
A molded body having a total volume fraction of these fine pieces of 62 to 95% is formed, and the molded body is poured into a molten metal of a light metal selected from the group consisting of Al, Al alloy, Mg, and Mg alloy as a matrix metal. A method for producing a metal matrix composite material, wherein the molten metal is allowed to penetrate into the molded body without substantially applying pressure. (2) Discrete reinforcing materials, fine pieces of Al or Al alloy with a volume fraction of 60-80%, and Ni, Cu with a volume fraction of 1-10%
or a fine piece of an alloy containing any of these as a main component or a mixture thereof, and a fine piece of Ti or a Ti alloy with a volume percentage of 1 to 10%, and the total volume of these fine pieces and the reinforcing material forming a molded body having a ratio of 62 to 95%, and using the molded body as a matrix metal of Al, Al alloy, M
g. A method for producing a metal matrix composite material, which comprises contacting a molten metal of a light metal selected from the group consisting of Mg alloys and allowing the molten metal to infiltrate into the molded body without substantially applying pressure.