JP2008075105A - Composite material and its production method - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a composite material in a simple method, improving the heat-resistance and the wear-resistance by reducing the remained metallic aluminum component to a minimum and also, showing the high strength by the dense structure, related to the composite material produced with a combustion-synthesis method (SHS:Self-propagating High-Temperature Synthesis). <P>SOLUTION: In the composite material 15 having a continuous phase of titanium-aluminum intermetallic compounds as the main component, the combustion-synthesis reaction is applied to mixed powder 12 containing metallic titanium powder (Ti) and ceramics powder (Al<SB>3</SB>Ti), and molten aluminum 11. <P>COPYRIGHT: (C)2008,JPO&INPIT

Description

  The present invention relates to a composite material manufactured by a combustion synthesis method (SHS: Self-propagating High-Temperature Synthesis) and a manufacturing method thereof.

The combustion synthesis method is a method of synthesizing a target substance by causing a chemical reaction in a chain by heat generated by a combustion reaction. In this way, the combustion synthesis method is a synthesis method that uses reaction heat, so it is possible to proceed with the synthesis of a substance without input of energy simply by setting the material to a temperature at which the combustion synthesis reaction is excited. Therefore, it is attracting attention from the viewpoint of energy saving.
However, in the combustion synthesis method, since the reaction is rapid and accompanied by a rapid temperature rise, problems such as expansion of the composite material to be generated are likely to occur, and it is difficult to control the reaction. For this reason, the difficulty of imparting desired characteristics to the composite material while stabilizing the combustion synthesis reaction is a drawback, and at present, industrial applications are not progressing.

In order to overcome such drawbacks and provide predetermined characteristics, there are known techniques as follows.
(1) Techniques for imparting dense and excellent bonding properties to a composite material by combining a pressurizing operation simultaneously with a combustion synthesis reaction are disclosed (for example, Patent Documents 1 and 2).
(2) A powder layer capable of combustion synthesis is provided on a base material made of an aluminum composite material. Further, a technique is disclosed in which a combustion synthesis reaction is caused to ceramicize (composite) the powder layer, and the reaction heat causes a combustion synthesis reaction at the interface between the base material and the powder layer to strengthen the bonding. (For example, Patent Document 3).
(3) In the method of obtaining a composite material containing an aluminide intermetallic compound by infiltrating molten aluminum to cause a combustion synthesis reaction, the penetration of aluminum is promoted by controlling the porosity and metal volume fraction, and the bond is strong A technique for imparting the following characteristics to a composite material is disclosed (for example, Patent Documents 4-7).
JP-A-9-71479 Japanese Patent Laid-Open No. 11-172351 JP-A-5-148614 Japanese Patent Laid-Open No. 2004-211109 JP 2004-346368 A JP 2004-307883 A JP 2004-353087 A

However, the techniques disclosed in Patent Documents 1 and 2 have a problem in that cracking and peeling are likely to occur because the shrinkage rate during sintering differs between the constituent materials of the composite material. Furthermore, since the pressurizing operation to the composite material is indispensable, there is a problem that the equipment becomes large-scale, and it becomes difficult to form a complicated shape or near net shape, and additional work is required. Further, there is a problem that it is difficult to combine the constituent materials having greatly different sintering temperatures.
Moreover, in the technique disclosed in Patent Document 3, since the reaction heat released by the combustion synthesis reaction is cooled by the base material, the reaction that contributes to the joining of the base material and the powder layer stops halfway, There is a problem that sufficient bonding strength cannot be obtained. If the reaction heat in combustion synthesis is increased to improve this, there is a problem that the powder layer becomes porous or expands and a composite material having the desired structure cannot be obtained.
And the technique currently disclosed by patent documents 4-7 raises temperature by the reaction heat by combustion synthesis, improves the wettability of molten aluminum, raises penetration power, fills the space between particles and particles, and is dense. This is a method for obtaining a composite material. However, since many metal aluminum components remain in the composite material structure of Patent Documents 4-7 (as well as Patent Documents 1-3), it melts when used as a sliding material in a high temperature / high load environment. There is a problem that the material is welded or worn, or the composite material itself is destroyed.
An object of the present invention is to solve such a problem, and to reduce the metal aluminum component remaining in the composite material as much as possible to improve heat resistance and wear resistance, and to make the structure dense and exhibit high strength Is intended to be provided by a simple method.

In order to solve the above problems, the present invention burns a composite material having a continuous phase mainly composed of a titanium-aluminum intermetallic compound, a mixed powder containing metal titanium powder and ceramic powder, and molten aluminum. A means of synthesis reaction is used.
When the invention comprises the above means, the first chemical reaction in which the titanium-aluminum intermetallic compound is generated from the metal titanium powder and the molten aluminum to generate heat when the molten aluminum penetrates into the mixed powder. This heat generation is used to generate a second chemical reaction in which an aluminum compound is generated from the ceramic powder and the remaining molten aluminum and absorbs heat.
As a result, the rapidity of the combustion synthesis reaction can be mitigated, and the metal aluminum component remaining in the composite material can be reduced.

Further, the ceramic powder has a mean particle diameter in the range of 1 to 3 μm, and the mixed powder has a molar ratio of the metal titanium powder and the ceramic powder to be mixed is 1: 3.5 to It is a means to be included in the range of 1:20.
When the invention is constituted by such means, it becomes possible to set the firing temperature necessary to excite the combustion synthesis reaction to 900 to 1200 ° C., which is much lower than before. Furthermore, the second chemical reaction between the ceramic powder and the molten aluminum is promoted, so that a composite material can be obtained which stabilizes the combustion synthesis reaction and has almost no remaining metallic aluminum component.

Further, the ceramic _{powder, TiO 2, NiO, SiO 2} , Nb 2 O 3, B 2 O 3, MnO, FeO, Fe 2 O 3, CuO, Cu 2 O, ZnO, TiN, Fe 4 N, Ca 3 Means include at least one of compounds selected from N ₂ and Mo ₂ N.
When the invention is constituted by such means, when the ceramic powder is a metal nitride, a dispersed phase containing aluminum nitride is formed in the continuous phase of the composite material. Further, when the ceramic powder is a metal oxide, a dispersed phase containing aluminum oxide is formed in the continuous phase of the composite material.

  According to the present invention, since the rapid reaction of the combustion synthesis reaction can be suppressed, the structure is densified and a high-strength composite material is provided. And since the metal aluminum component remaining inside can be reduced as much as possible, a composite material having high heat resistance and high wear resistance is provided. Such a composite material can be provided by a simple method.

The present invention will be described with reference to the drawings.
FIG. 1 is a process diagram of a method for producing a composite material showing an embodiment of the present invention.
As shown to Fig.1 (a), the mixed powder 12 is spread in the crucible 13, and also solid aluminum (Al ingot 11) is installed on it.
Here, the mixed powder 12 contains at least metal titanium powder (hereinafter referred to as Ti powder) and ceramic powder (TiN). The mixed powder 12 is tapped and spread in the crucible 13, but may be compacted in advance and placed on the bottom surface.

As shown in FIG.1 (b), the crucible 13 is installed in the baking furnace 14 which can make Al ingot 11 contact-position on the mixed powder 12, and can heat these uniformly. The firing furnace 14 melts the Al ingot 11 and supplies energy necessary for exciting a combustion synthesis reaction described later.
Thus, the interface portion between the Al ingot 11 and the mixed powder 12 immediately after being set in the firing furnace 14 is adjacent to the adjacent Ti powder and TiN powder as shown in the conceptual view of the cross section in FIG. It has a moderate gap.

As shown in FIG. 1 (c), the firing temperature T of the firing furnace 14 is set to be equal to or lower than the melting temperature of Al ₃ Ti (titanium-aluminum intermetallic compound) to be produced later and equal to or higher than the melting temperature of the Al ingot 11. Then, a part of the Al ingot 11 melts, and as shown in FIG. 1 (g), the molten aluminum fills the continuous gap between the Ti powder and TiN powder and mixes as shown in FIG. 1 (d). It penetrates the entire powder 12.

Thus, in the process of filling molten aluminum, the combustion synthesis reaction as shown in the following reaction formulas (1) and (2) proceeds. Reaction formula (1) is an exothermic reaction in which molten aluminum and Ti powder generate a chemical reaction (hereinafter referred to as “first chemical reaction”) to produce Al ₃ Ti (a titanium-aluminum intermetallic compound). And this 1st chemical reaction occurs in a chain, and molten aluminum permeates the mixed powder 12 instantly. Further, the gap between the Ti powder and the TiN powder is replaced with a continuous phase mainly composed of Al ₃ Ti (titanium-aluminum intermetallic compound).

<Combustion synthesis reaction>
3Al + Ti → Al ₃ Ti + 146 kJ (1)
Al + TiN + 20 kJ → AlN + Ti (2)

As shown in FIG. 1 (h) and reaction formula (2), the molten aluminum and TiN (ceramic powder) remaining using the exothermic heat of the first chemical reaction are subjected to a chemical reaction (hereinafter referred to as “second chemical reaction”). ”) To generate AlN (aluminum compound) and absorb heat. In the first place, there is an effect of improving the heat mass due to the presence of TiN, and furthermore, this endotherm suppresses a rapid temperature rise due to the first chemical reaction (exotherm), and thus the entire combustion synthesis reaction proceeds stably. . Further, since the firing temperature T in the firing furnace 14 is set lower than the melting temperature of Al ₃ Ti (titanium-aluminum intermetallic compound) that forms the continuous phase, the composite material 15 is of good quality without expanding. Things are obtained.
The metal titanium (Ti) generated in the second chemical reaction (reaction formula (2)) is changed to Al ₃ Ti (titanium-aluminum intermetallic compound) by the reaction formula (1).

As shown in FIG. 1 (e), the composite material 15 produced after the completion of the combustion synthesis reaction is returned to room temperature and then removed from the crucible 13. FIG. 1I is a cross-sectional view of the composite material 15 observed with a microscope. Thus, the composite material 15 includes a continuous phase mainly composed of Al ₃ Ti (titanium-aluminum intermetallic compound) generated by the first chemical reaction (exotherm) and AlN (generated by the second chemical reaction (endothermic)). It can be seen that it has a dense structure formed from a dispersed phase in which an aluminum compound) and unreacted TiN (ceramics powder) are uniformly dispersed, and almost no metallic aluminum remains.
In the embodiment, the composite material 15 shows a material in which the residual aluminum phase and the composite phase are separated into two layers. However, the composite material 15 is not limited to such a form. In the case where is partially dispersed, the case where the residual aluminum phase and the composite phase are entirely dispersed is also included.

Next, the optimum mixing ratio of Ti powder and TiN (ceramic powder) in the mixed powder will be examined with reference to FIG.
FIG. 2 shows curve (A, B, C, D) of reaction temperature at each mixing ratio of the mixed powder (Ti / TiN) when the firing temperature T is set to 900 ° C., 1000 ° C., 1200 ° C., 1400 ° C. Respectively.
These reaction attainment temperature curves A, B, C, and D are theoretical curves derived from the change in reaction enthalpy at each mixing ratio of the mixed powder (Ti / TiN).

By the way, as described above, in order to cause a chain combustion synthesis reaction stably, the reaction arrival temperature of the mixed powder (Ti / TiN) is lower than the melting temperature of Al ₃ Ti (titanium-aluminum intermetallic compound). And the melting temperature of the Al ingot 11 needs to be higher than the melting temperature. That is, as shown in the stable reaction zone E in FIG. 2, the mixed powder (Ti) so that the reaction reaching temperature curves A, B, C, and D are included in the Al flow zone and the Al ₃ Ti fixed zone. / TiN) needs to be set.

FIG. 3 is a graph showing a differential thermal analysis (DTA) result of a mixture of mixed powder and metal Al. FIG. 3A shows a mixed powder having a mixing ratio of Ti-90 volume% TiN, and FIG. 3B shows a Ti-95 volume% TiN.
From this DTA measurement result, the excitation temperature of the combustion synthesis reaction that forms the titanium-aluminum intermetallic compound can be certified. That is, from FIGS. 3A and 3B, since exothermic peaks are observed in the vicinity of 885 ° C. and 835 ° C., respectively, this temperature range can be recognized as the excitation temperature of the combustion synthesis reaction. Although the explanation was mixed, the reason why the firing temperature T is set to 900 ° C. or higher in the reaction arrival temperature curves A, B, C, and D in FIG. 2 is to be set higher than the excitation temperature of the combustion synthesis reaction. Because there is.

  Further, it becomes possible to qualitatively analyze the rapidity of the combustion synthesis reaction in each composition of the mixed powder from the peak shape of the DTA curve at this excitation temperature. Comparing the peak shapes of the DTA curves in FIG. 3A and FIG. 3B, it can be said that the former peak has larger intensity and area. That is, as the mixing ratio of TiN (ceramic powder) in the mixed powder increased, the result was that the rapidity of the combustion synthesis reaction was suppressed. It can be said that this result is consistent with the combustion synthesis reaction (reaction equations (1) and (2)) described above and the experimental results described later with reference to FIG.

  In the table shown in FIG. 4A, the firing temperature T of the firing furnace 14 (see FIG. 1) is set in the range of 800 to 1400 ° C., and the Ti / TiN mixing ratio is in the range of 0 to 100% of the Ti mixing ratio. It is a table | surface which shows the result of having carried out the combustion synthesis reaction by changing and evaluating the stability of the reaction. Among these, about the result of the condition setting which attached the sandy pattern, the whole observation photograph of the cross section in FIG.4 (b) was published in the microscope observation photograph of the partial cross section in FIG.4 (c).

As shown in FIG. 4A, the result of the TiN mixing ratio of less than 80% indicates an unstable reaction (x1, x2, x3) regardless of the firing temperature. Among these, in the condition setting indicated by (× 3), as shown in the corresponding whole observation photograph of FIG. 4B, the shape of the composite material is greatly deformed by the reaction, or a porous state is seen inside. It was.
As shown in FIG. 2, the reason why this occurs is that, when the mixing ratio of TiN is less than 80%, it is suggested that all the reaction temperature curves AD are in the flow region of Al ₃ Ti. That is, in a composition having a TiN mixing ratio of less than 80%, the combustion synthesis reaction is rapidly excited, and the temperature becomes so high that Al ₃ Ti constituting the continuous phase of the composite material flows. The same reason is considered to be the unstable reaction in which the result of the TiN mixing ratio of 0% shows rapid expansion (× 1).

In addition, in FIG. 4A, the result of the firing temperature T of 800 ° C. shows an unstable reaction (× 2) that is only partially subjected to the combustion synthesis reaction regardless of the TiN mixing ratio. This is because the excitation temperature at which the metal Ti powder and molten aluminum undergo a combustion synthesis reaction is higher than 800 ° C. (835 ° C., 885 ° C.) as shown in FIG. The
That is, it is considered that when the firing temperature is 800 ° C., the combustion synthesis reaction is not excited, so that the molten aluminum does not penetrate into the mixed powder.
In addition, even when the TiN mixing ratio is larger than 96% (1:20 in molar ratio), the unstable reaction (partial reaction (× 2), non-penetrated state (× 4)) is partially due to combustion synthesis reaction Even so, it is considered that the reaction temperature does not reach the excitation temperature, and the chain reaction does not proceed. For this reason, it is considered that molten aluminum cannot penetrate into the ceramic powder (TiN).

On the other hand, in FIG. 4A, when the firing temperature is 900 ° C. to 1200 ° C. and the TiN mixing ratio is 93% to 96%, the stable reaction is such that the residual aluminum phase and the composite phase show clear separation. (See the overall observation photograph corresponding to ◎ in FIG. 4B). Moreover, from the micrograph corresponding to the stable reaction の う ち in FIG. 4C, it can be seen that the structure of the composite layer is very dense. However, it can be said that as the firing temperature T increases, the extent to which the Al ₃ Ti component is dispersed in the residual aluminum increases.
Further, in FIG. 4A, when the firing temperature is 1400 ° C. and the TiN mixing ratio is 80% to 96%, a stable reaction Δ is shown such that the residual aluminum phase and the composite phase are dispersed as a whole (FIG. 4). (See the overall observation photograph corresponding to Δ in 4 (c)).

From the above results, the mixed powder 12 (see FIG. 1) has a molar ratio of the metal titanium powder (Ti) to be mixed and the ceramic powder (TiN) of 1: 3.5 to 1:20 (mixing ratio of the ceramic powder). In the range of 80% to 96%).
When the molar ratio is less than 1: 3.5, which is the lower limit of the above range, the combustion synthesis reaction becomes unstable to the extent that the composite material 15 exhibits a porous state. In addition, in the range exceeding the molar ratio 1:20 which is the upper limit of the above range, the combustion synthesis reaction becomes unstable to such an extent that the composite material 15 exhibits a partial reaction or an unpermeated state.

FIG. 5 is a graph in which a test piece made of an embodiment of the present invention (Example), cast iron FC250 (Comparative Example 1), and a metal aluminum material (Example 2) was prepared and the sliding heat resistance limit was evaluated by a drag test. is there.
The experimental conditions were such that a torque of 5 kg · m was applied, the rotation speed of the rotating plate was 500 rpm, and a phenol resin composite material was used as the counterpart material.
As a result, the product according to the present invention (Example) showed surface heat resistance at an ultimate temperature of 747 ° C., and almost the same result as the surface heat resistance (final temperature 797 ° C.) of cast iron FC250 (Comparative Example 1) was obtained. It was. In addition, the product of the present invention (Example) obtained results superior to the surface heat resistance (attainment temperature 501 ° C.) of metal aluminum (Comparative Example 2).
The composite material of the product of the present invention has such a high temperature / high strength performance because it has a continuous layer mainly composed of a titanium-aluminum intermetallic compound having excellent high temperature characteristics, and the structure is densified. It seems to be related.

Next, the optimum range of the particle diameter of the ceramic powder (TiN) necessary for favoring the combustion synthesis reaction will be examined.
In the table shown in FIG. 6, the conditions are changed within the ranges of the firing temperature (900 to 1400 ° C.), the particle diameter of metal titanium powder (Ti) (45 to 250 μm), and the particle diameter of ceramic powder (TiN) (1 to 53 μm). 3 is a table showing the evaluation of reaction stability after combustion synthesis reaction.
From this result, the ceramic powder has an average particle size in the range of 1 to 3 μm, more preferably 1 to 1.5 μm.

  If the average particle size is less than the lower limit of 1 μm, TiN aggregates around the Ti powder and inhibits the contact between Al and Ti, so that the first chemical reaction (exotherm) described above is suppressed and chain combustion occurs. It is thought that the synthesis reaction is not satisfactory. On the other hand, if the average particle size is larger than the upper limit of 3 μm, it is considered that the effective area where the molten aluminum and the ceramic powder are in contact with each other decreases. As a result, it is considered that the second chemical reaction (endotherm) described above is suppressed and the first chemical reaction (exotherm) proceeds rapidly.

Next, other materials that can be applied in addition to TiN as a ceramic powder to be mixed with the mixed powder 12 (see FIG. 1) will be examined.
The table shown in FIG. 7 shows metal oxides (Al ₂ O ₃ , SiO ₂ , TiO ₂ , ZrO ₂ , CaO, MgO, NiO) and metal nitrides (BN, TiN) as ceramic powders mixed with the mixed powder. It is the table | surface which evaluated the reaction stability of the combustion synthesis reaction when applied. In the visual evaluation, ◯ indicates a healthy non-defective product, Δ indicates that there is a partially unpermeated portion of the molten aluminum, and × indicates that the reaction has violently expanded.
Further, a titanium-aluminum intermetallic compound (Al ₃ Ti) that is generated by the first chemical reaction (exothermic heat) and forms the continuous phase of the composite material, and an aluminum system that is generated by the second chemical reaction (endothermic heat) and forms the dispersed phase. X-ray diffraction spectroscopy (XRD) results showing the composition ratio of the compound (Al ₂ O ₃ , AlN...), The ceramic powder constituting the disperse phase without reaction and the residual aluminum (Al). It also shows.

From the viewpoint of the above-described sliding heat resistance, it is preferable that a large amount of titanium-aluminum intermetallic compound (Al ₃ Ti) is contained in the composite material and a small amount of Al is detected. Moreover, it can be said that it is preferable that a 2nd chemical reaction (endothermic) is advanced and many aluminum compounds are produced | generated from a viewpoint of making a combustion synthesis reaction progress stably.
Therefore, in XRD analysis, those with a high Al content and a small amount of aluminum compounds (for example, FIGS. 7 (6) (7) (8)) are combusted and synthesized because the second chemical reaction (endotherm) is rare. It was suggested that the reaction was unstable, and knowledge that coincided with the visual evaluation result (Δ) of the permeation reaction was obtained.

From the evaluation results shown in this FIG. 7 and the experimental results omitted from the description, the ceramic powder is not only TiN shown in the embodiment, but also Fe ₄ N, Ca ₃ N ₂ , Mo ₂ N, and TiO which is a metal oxide. ₂ , NiO, SiO ₂ , Nb ₂ O ₃ , B ₂ O ₃ , MnO, FeO, Fe ₂ O ₃ , CuO, Cu ₂ O, ZnO and other compounds were found to be effective. Moreover, the knowledge that selecting and applying a plurality of these compounds was also obtained.

  As described above, in the present invention, the metal aluminum component remaining in the composite material is reduced as much as possible, so that the heat resistance and wear resistance of the composite material can be enhanced. Furthermore, since this composite material has a dense structure, it exhibits high strength. In addition, since the combustion synthesis method (SHS) can be performed without using special equipment, the composite material can be provided by a simple method.

(A)-(e) is process drawing of the manufacturing method of the composite material which shows embodiment of this invention, (f)-(h) is a conceptual diagram of the cross section of the composite material in each process, (i ) Is a SEM observation view of the cross section of the composite material in the final step. When a calcination temperature is set to 900 degreeC, 1000 degreeC, 1200 degreeC, and 1400 degreeC, it is a graph which respectively shows the reaction ultimate temperature in the mixing rate of mixed powder (Ti / TiN) as a curve. It is a graph which shows the differential thermal analysis (DTA) result of the mixture of the mixed powder which shows the mixing rate of (a) Ti / 90 volume% TiN (b) Ti / 95 volume% TiN, and metal Al. It is a table showing the evaluation of reaction stability by changing the conditions within the range of firing temperature (800 to 1400 ° C.) and Ti / TiN mixing ratio (Ti mixing ratio 0 to 100%). Shows a stable reaction that shows a clear separation between the phase and the composite phase, ○ shows a stable reaction that the composite phase is partially dispersed in the residual aluminum phase, and △ shows that the residual aluminum phase and the composite phase are totally dispersed X1 indicates an unstable reaction such that the composite material rapidly expands, and x2 indicates an unstable enough that the combustion synthesis reaction is only partially excited in the composite material. X3 shows an unstable reaction to the extent that the composite material shows a porous state, and x4 shows an unstable reaction to the extent that molten aluminum hardly penetrates into the ceramic powder (TiN). It is the graph which produced the test piece which consists of the implementation goods (Example) of this invention, cast iron FC250 (comparative example 1), and a metal aluminum material (Example 2), and evaluated the sliding heat-resistant limit property by a drag test. It is formed by changing the conditions within the range of firing temperature (900-1400 ° C), metal titanium powder (Ti) particle size (45-250 µm), and ceramic powder (TiN) particle size (1-53 µm). It is a table | surface which shows evaluation of the composite material made. Combustion synthesis reaction when metal oxide (Al ₂ O ₃ , SiO ₂ , TiO ₂ , ZrO ₂ , CaO, MgO, NiO) or metal nitride (BN, TiN) is applied as the ceramic powder mixed with the mixed powder It is the table | surface which evaluated reaction stability of. Furthermore, the titanium-aluminum intermetallic compound (Al ₃ Ti) constituting the continuous phase of the composite material, the ceramic powder constituting the dispersed phase, the aluminum-based compound also constituting the dispersed phase, and the residual aluminum (Al) An X-ray diffraction analysis (XRD) result representing the composition ratio is also shown.

Explanation of symbols

11 Al ingot (solid aluminum, molten aluminum)
12 Mixed powder 14 Firing furnace 15 Composite material

Claims (5)

In a composite material having a continuous phase mainly composed of a titanium-aluminum intermetallic compound,
A composite material obtained by subjecting a mixed powder containing a metal titanium powder and a ceramic powder and a molten aluminum to a combustion synthesis reaction. The composite material according to claim 1, wherein
The ceramic powder includes an average particle size in the range of 1 to 3 μm. The composite material according to claim 1 or 2,
The mixed powder is a composite material in which a molar ratio of the metal titanium powder and the ceramic powder to be blended is included in a range of 1: 3.5 to 1:20. In the composite material according to any one of claims 1 to 3,
The ceramic powder includes TiO ₂ , NiO, SiO ₂ , Nb ₂ O ₃ , B ₂ O ₃ , MnO, FeO, Fe ₂ O ₃ , CuO, Cu ₂ O, ZnO, TiN, Fe ₄ N, and Ca ₃ N _2. A composite material comprising at least one compound selected from Mo ₂ N. In the method for producing a composite material having a continuous phase mainly composed of a titanium-aluminum intermetallic compound,
A step of bringing solid aluminum into contact with a mixed powder containing metal titanium powder and ceramic powder;
Setting the firing temperature below the melting temperature of the titanium-aluminum intermetallic compound and above the melting temperature of the solid aluminum;
Infiltrating the molten aluminum in which the solid aluminum is melted into the mixed powder;
The metal titanium powder and the molten aluminum undergo a first chemical reaction to generate the titanium-aluminum intermetallic compound and generate heat;
A method of producing a composite material, comprising: a step of utilizing the heat generation to generate an aluminum compound by the second chemical reaction between the ceramic powder and the remaining molten aluminum to absorb heat.