JPH0585272B2 - - Google Patents

Description

[Detailed description of the invention]

INDUSTRIAL APPLICATION FIELD The present invention relates to surface treatment of metal materials, and more particularly to a method for forming a ceramic particle-dispersed metal composite layer on the surface of a metal material. Conventional technology As a means of improving the wear resistance, heat resistance, corrosion resistance, etc. of metal materials such as steel, ceramic particles, which themselves have high strength and hardness and have excellent heat resistance and corrosion resistance, are incorporated into metal materials. It is known to be effective to disperse and thereby form ceramic particle-dispersed metal composite materials or composite layers. Thus, as a method for dispersing ceramic particles in a metal material, a supersaturated solid solution is formed by performing solution treatment on a metal material containing a solid solution forming element such as a metal carbide, and the supersaturated solid solution is dispersed in a predetermined manner. A precipitation hardening method in which a solid solution is aged and precipitated by holding it at a temperature for a certain period of time, and a metal material containing a metal element that is more reactive with oxygen than the base metal is maintained at a specified temperature for a certain period of time in an oxidizing atmosphere. An internal oxidation method in which oxygen is diffused from the surface of the metal material to the inside thereof to oxidize the element inside the metal material, and the ceramic powder to be dispersed and the base metal powder are mixed, and the mixing A powder metallurgy method (sintering method) in which powder is compression molded and the compression molded body is heated to a high temperature, ceramic powder dispersed in a molten base metal is added and stirred, and the mixture thus obtained is Compocasting methods for casting molten metal have been known for some time. Problems to be Solved by the Invention In the precipitation hardening method described above, it is possible to disperse extremely fine dispersed particles in the base metal, and a composite material with excellent adhesion between the dispersed particles and the base metal can be created. However, it is difficult to properly control the volume fraction, size, etc. of the dispersed particles, and the aging treatment requires heating and maintaining the metal material at a predetermined temperature for a long time, such as over 10 hours. However, since it is necessary to process the entire metal material, it is difficult to form a ceramic particle-dispersed metal composite layer inexpensively and efficiently, and it is difficult to form a ceramic particle-dispersed metal composite layer only on a specific surface. It is difficult to manufacture metal materials with In addition, in the internal oxidation method, the metal material to be treated must contain a metal element that is more reactive with oxygen than the base metal, and the metal material must be kept at high temperatures near its melting point for a long time. Since heating must be maintained for a period of time, it is difficult to efficiently and inexpensively form an oxide-based ceramic particle-dispersed metal composite layer on the surface of the metal material. In addition, with this method, it is impossible to disperse non-oxide ceramic particles in the base metal, and it is difficult to appropriately control the volume fraction, size, etc. of the oxide ceramic particles. It is. Furthermore, in the powder metallurgy method, although it is possible to control the volume fraction, size, shape, etc. of ceramic particles relatively easily, it is difficult to form a ceramic particle-dispersed metal composite layer only on a specific surface area of the metal material. Therefore, it is difficult to easily and inexpensively form a ceramic particle-dispersed metal composite layer on a specific surface portion of a metal material. Furthermore, it is extremely difficult to form a ceramic particle-dispersed metal composite layer with substantially zero porosity or a ceramic particle-dispersed metal composite layer with excellent adhesion between the ceramic particles and the base metal. Furthermore, in the composite cast method, although it is possible to easily produce a casting made of a ceramic particle-dispersed metal composite material, it is extremely difficult to form a ceramic particle-dispersed metal composite layer only on a specific surface area of the metal material. It is difficult to form a composite layer in which ceramic particles are uniformly dispersed, and it is very difficult to properly control the volume fraction of ceramic particles in the composite layer. In view of the above-mentioned problems in the conventional method of dispersing ceramic particles in metal materials, the present invention has been developed to disperse ceramic particles of any type, such as oxide, nitride, or carbide, uniformly at a desired volume percentage. The object of the present invention is to provide a method that can easily form a dispersed ceramic particle-dispersed metal composite layer on a desired surface of a metal material. Means for Solving the Problems According to the present invention, the above-mentioned object is achieved by arranging a powder of a metal element having higher reactivity with oxygen than the main constituent elements of the metal material on the surface of the metal material; The highly reactive metal is dispersed in the surface layer of the metal material by heating and melting the powder and the surface layer of the metal material with a high-density energy source, and the surface layer is placed in an oxidizing gas atmosphere. A method for forming a ceramic particle-dispersed metal composite layer by heating the ceramic particle-dispersed metal composite layer, in which a powder of a metal element having higher reactivity with nitrogen than the main constituent elements of the metal material is placed on the surface of the metal material, and the powder and the surface of the metal material are Ceramic particle-dispersed metal in which the highly reactive metal is dispersed in the surface layer of the metal material by heating and melting the layer with a high-density energy source, and the surface layer is heated in a nitriding gas atmosphere. A method for forming a composite layer, and a powder of a metal element having higher reactivity with carbon than the main constituent elements of the metal material is placed on the surface of the metal material, and the powder and the surface layer of the metal material are heated with a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer comprising dispersing the highly reactive metal in the surface layer of the metal material by heating and melting the metal material, and heating the surface layer in a carbonizing gas atmosphere. It is achieved by doing so. Effects and Effects of the Invention According to the method of the present invention, powder of a metal element that is more reactive with oxygen, nitrogen, or carbon than the main constituent elements of the metal material is arranged on the surface of the metal material,
The metal powder and the surface layer of the metal material are locally heated to a high temperature by a high-density energy source and melted (including a semi-molten state), and the highly reactive metal is deposited in the surface layer of the metal material. After that, the surface layer of the metal material is heated in an oxidizing gas atmosphere, a nitriding gas atmosphere, and a carbonizing gas atmosphere, so that the dispersed highly reactive metals are oxidized and nitrided. The oxide, nitride, or carbide of the metal, that is, the oxide-based, nitride-based, or carbide-based ceramic is formed in a dispersed state. By using a metal powder of a certain size, ceramic particles of a desired type and size can be incorporated into a matrix metal consisting of a metal constituting the metal material or an alloy of the metal with a highly reactive metal at a desired volume percentage. A uniformly dispersed composite layer can be easily formed on a specific surface of the metal material, and in this case, the surface of the metal material is also partially melted, so it has excellent integrity with the metal material. Composite layers can be formed. Furthermore, according to the method of the present invention, the ceramic particles dispersed as in the internal oxidation method are not limited to oxide-based ceramic particles, and are highly reactive in relation to the main constituent elements of the metal material. By appropriately selecting the metal element, in addition to improving properties such as wear resistance due to ceramic particle dispersion, properties such as corrosion resistance can also be improved by changing the composition of the matrix metal of the composite layer. According to one detailed feature of the method of the present invention, the metal powder and the surface layer of the metal material melted by the high-density energy source are rapidly cooled mainly due to heat absorption by the main part of the metal material, i.e., the parts other than the surface layer. be done. According to such a method, a special cooling device for cooling the molten metal powder and the surface layer of the metal material is not required. According to another detailed feature of the method of the invention, the step of heating and melting the metal powder and the surface layer of the metal material with a high-density energy source is carried out in an inert atmosphere. According to this method, it is possible to avoid problems such as oxidation of metal powder and the like and oxidation of the matrix metal of the composite layer. In this case, the inert atmosphere may be created using flux as in the case of welding, but from the viewpoint of reliability, avoidance of slag entrainment, and workability, an inert gas atmosphere such as argon or helium or a vacuum atmosphere may be used. It is preferable that there be. Further, the high-density energy source in the method of the present invention may be a laser, a TIG arc, or an electron beam, but the laser can also be applied when the electrical resistance of the metal powder or metal material is relatively high, and the TIG is superior to other high-density energy sources in that the size of the heating range for the surface layer of metal powder and metal materials can be adjusted relatively easily through adjustment.
Arc and electron beams are superior to lasers in that when metal powder or the like is melted, the molten metal is stirred by electromagnetic stirring. Furthermore, while the atmosphere for electron beams generally must be a vacuum atmosphere, the atmosphere for lasers and TIG arcs may be an inert gas atmosphere, so the equipment and work efficiency necessary to create and maintain the specified atmosphere are Lasers and TIG arcs are preferred from this point of view, whereas electron beams have a very small heating area and can achieve large penetration depths, making them superior to other high-density energy sources when such characteristics are required. . Therefore, according to yet another detailed feature of the method of the invention, depending on the type of metal powder, the shape, area, thickness, etc. of the composite layer to be formed, a laser, TIG, etc. can be used as the high-density energy source. Arc and electron beam can be used as appropriate. Further, in the method of the present invention, the atmospheric gas when heating the surface layer of the metal material in a predetermined atmosphere is a mixed gas of an oxidizing gas, a nitriding gas, or a carbonizing gas and an inert gas. For example, oxidizing gas is a mixture of oxygen and an inert gas such as argon, nitriding gas is a mixture of ammonia and an inert gas such as nitrogen, and carbonizing gas is a mixture of carbon monoxide, carbon dioxide, etc. It is a mixed gas with an inert gas such as nitrogen. According to this method, a highly reactive metal dispersed in the surface layer of a metal material is oxidized,
The degree of nitriding or carbonization can be appropriately controlled. Furthermore, in this case, the substance forming the atmospheric gas does not have to be a gas itself; it can be a solid substance as long as it can dissociate into the atomic state of oxygen, nitrogen, or carbon when heated to a predetermined high temperature. It may be hot. The metal powder used in the method of the present invention may be a single type of metal powder or a mixed powder of multiple types of metal powder. For example, metals that are more reactive with oxygen than Fe are Si, Cr, Ti, V, Zr, Al, Mg,
There are metals such as Mo, Mn, Ta, and W, and metals that are more reactive with nitrogen than Fe are Si, Cr, Ti, Zr,
Al, Mg, Mo, Ta, etc., and metals that are more reactive with carbon than Fe are Si, Cr, Ti,
There are V, Zr, Al, Mo, Mn, Ta, Nb, W, etc., and the reaction formula of these metal elements with oxygen, nitrogen, and carbon, and the standard freedom when forming oxides, nitrides, and carbides at 1500K. The changes in energy △G゜ are as shown in Tables 1 to 3 below, and the highly reactive metal element in the method of the present invention can be selected from any of the metal elements mentioned above. Preferably,
The main constituent element of the metal material is preferably a metal element other than the above-mentioned metal elements.

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[Table] Also, according to the results of experimental research conducted by the inventors of the present invention, it is possible to easily melt the surface layer of metal powder and metal materials, and to prevent the formation of pores in the alloy layer thus formed. In order to achieve this, the average particle size of the metal powder is preferably 300μ or less, particularly 100μ or less. Further, placing the metal powder on the surface of the metal material may be performed by simply pre-arranging the mixed powder in a layer on the surface of the metal material, or when the high-density energy source is a laser or an electron beam. This may be carried out by continuously feeding metal powder onto the surface of the metal material at a position in front of a high-density energy source in the scanning direction, but this method prevents the metal powder from scattering and improves its yield. In order to
A compacted body of metal powder is placed on a metal material, grooves are formed on the surface of the metal material and the metal powder is compacted in the grooves, or an aqueous solution of PVA (polyvinyl alcohol) or an aqueous solution of PVA (polyvinyl alcohol) is applied to the metal powder. A binder such as a mixture of cellulose and glycerin is added to form a base, and the base is attached to the surface of a metal material by a spatula coating method or a tube method, or the thickness of the composite layer to be formed is determined. If a small amount is acceptable, metal powder is dispersed in a solvent such as a solvent prepared by dissolving acrylic resin with thinner to form a slurry.
The slurry may be applied to the surface of the metal material by applying with a brush, spraying, or dipping. However, when a paste or slurry is formed, the baset or slurry will not oxidize the surface of the metal powder layer formed by drying them, nor will pores etc. be generated on the surface of the alloy layer. It is preferable that the material be sufficiently dried in a temperature range and atmosphere and heated with a high-density energy source in a substantially moisture-free state. 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 By preparing chromium powder (purity 99.5%) with an average particle size of 50μ and injecting a 5% aqueous solution of polyvinyl alcohol as a binder into the chromium powder,
It formed a paste that was more viscous than water and less viscous than clay. Then, as shown in Figure 1, 70 x 40 x 10
A specimen 1 made of tool steel (JIS standard SKD61) with dimensions of Arranged parallel to each other with a distance of 5 mm,
Paste 4 was filled between these guides using a spatula coating method, so that a base material was arranged in a layer having a width of 5 mm and a thickness of 0.5 mm along the longitudinal direction at the center of the surface of the test piece. Next, although not shown in the figure, the test piece was kept at 100℃ for 0.5 hours in a drying oven to sufficiently dry the paste, which resulted in a porosity of about 40% as shown in Figure 2. A chromium powder layer 5 was formed on the specimen 1. Next, as shown in FIG. 3, argon is emitted as a shielding gas from the tip of the TIG torch 6, thereby shielding the molten part on the test piece while TIG is applied from one end of the chromium powder layer 5 to the other.
By scanning the torch 6 in one pass, the chromium powder layer is locally heated by the TIG arc 7 under the conditions shown in Table 4 below to melt the chromium powder and the surface of the test piece. An alloy layer 8 made of an iron alloy in which particles were dispersed was formed. In this case, the alloy layer and the heated surface portion of the test piece were rapidly cooled due to heat absorption mainly by the main part of the test piece. Table 4 Current: 120A Voltage: 25V Polarity: DC rod positive electrode: Tungsten Scanning speed: 3.0mm/sec Arc length: 7.5mm Argon flow rate: 5/min Next, as shown in Figure 4, test piece 1 was placed on the mounting table 10 in the reaction container 9, and the test piece 1
A mixed powder 11 of iron powder and ferric oxide powder is placed on the mounting table 10 around the reaction vessel 9, and then a mixed gas of argon and oxygen (mixing ratio 9:
1) was replaced. Next, the inside of the reaction vessel 9 was heated to 1300°C for 5 hours by the heater 12 placed around it, thereby causing the reaction of Fe ₂ O ₃ →2Fe+3/2O ₂ 3/2O ₂ →3O 2Cr+3O→Cr ₂ O ₃ ( Oxygen in the second equation above is also supplied by gas in the atmosphere) to oxidize the chromium particles in the alloy metal,
As shown in the figure, a composite layer 15 made of an iron alloy 14 in which chromium oxide particles 13 were dispersed was formed. The width of the composite layer 15 formed as described above is 6.8 mm.
The maximum thickness was 1.9 mm. Furthermore, when we observed the cross section of the longitudinal center of the test piece, we found that there was a heat-affected zone 17 between the composite layer and the base metal 16 of the test piece, as schematically shown in FIG. However, the width was approximately 1.8 to 2.0 mm. In addition, the volume fraction of chromium oxide particles in the composite layer is approximately 3%, which is substantially uniform over the entire composite layer. It was also observed that the integrity was good. Furthermore, the average particle size of the chromium oxide particles was about 1 μ. FIG. 6 is an optical micrograph showing the metal structure at the center of the longitudinal cross-section of the composite layer 15 at 800 times magnification. In the figure, the light gray background is the iron alloy as the matrix metal, and the fine gray dots are chromium oxide particles. From FIG. 6, it can be seen that very fine and uniformly sized chromium oxide particles are uniformly dispersed in the matrix metal, and no defects such as pores are generated. Example 2 Titanium powder with an average particle size of 44μ (purity 99.0%)
A test piece having the same dimensions and the same material as the test piece used in Example 1 was also prepared. Then, as shown in FIG.
is placed below the laser gun 19 and the powder supply hopper 20, and the titanium powder 2 is placed in the powder supply hopper.
1 and introduced argon as a carrier gas into the powder supply hopper 20 while ejecting argon from the tip of the laser gun 19, thereby depositing titanium powder in the longitudinal direction at the center of the 70 x 40 mm surface of the test piece 18. By continuously feeding the test piece 18 and moving the test piece 18 to the right in the figure in this state,
By forming a titanium powder layer 22 on the surface of the test piece 18 and irradiating the titanium powder layer 22 with a laser, the titanium powder is locally heated by the laser under the conditions shown in Table 5 below. The titanium powder and the surface portion of the test piece were melted, thereby forming an alloy metal 24 made of an iron alloy in which titanium particles were dispersed. In this case, the formed alloy layer and the heated surface portion of the test piece were rapidly cooled mainly due to heat absorption by the main part of the test piece. Table 5 Power density: 210 W/mm ² Energy density: 200 J/mm ² Scanning speed: 3.6 mm/sec Next, as shown in FIG. A mixed gas of ammonia and nitrogen (mixing ratio 2:3) was introduced into the reaction container as an atmospheric gas while discharging air from inside the reaction container, thereby replacing the inside of the reaction container with a nitriding atmosphere. Next, the inside of the reaction vessel is heated by the heater 27 arranged around the reaction vessel 25.
Heating at 1250°C for 6 hours causes a reaction of NH ₃ → 1/2N ₂ + 3/2H ₂ 1/2N ₂ →N Ti+N → TiN to nitride the titanium particles in the alloy layer, resulting in titanium nitride. A composite layer 28 made of an iron alloy in which particles were dispersed was formed. The width of the composite layer 28 formed as described above is 5.8
mm, and the maximum thickness was 0.2 mm. In addition, when we observed the cross section of the longitudinal center of the test piece, we found that
As in Example 1, a heat affected zone existed between the composite layer and the base metal of the test piece, but the width was approximately 0.8 to 1.0 mm. In addition, the volume fraction of titanium nitride particles in the composite layer is approximately 5%, which is substantially uniform over the entire composite layer, and the adhesion between the titanium nitride particles and the iron alloy as the matrix metal and the relationship between the composite layer and the specimen. It was also observed that the integrity was good. Furthermore, the average particle size of the titanium nitride particles was 0.8μ. FIG. 9 is an optical micrograph showing the metal structure at the center of the longitudinal cross-section of the composite layer at 800 times magnification. In the figure, the light gray area is the iron alloy as the matrix metal, and the black dotted area is the titanium nitride particles. This eighth
From the figure, it can be seen that fine and uniformly sized titanium nitride particles are substantially uniformly dispersed in the matrix metal, and defects such as pores are not generated at all. Example 3 Titanium powder with an average particle size of 44μ (purity 99.0%)
and tungsten powder with an average particle size of 4μ (95% purity)
These powders were uniformly mixed to form a mixed powder in which the weight ratio of these powders was 1:1. A viscous paste similar to that in Example 1 was then formed by injecting a 5% aqueous solution of polyvinyl alcohol as a binder into the mixed powder. Next, a test piece of the same size and material as the test piece used in Example 1 was prepared, and in the same manner as in Example 1, a test piece was placed in the center of one of the 70 x 40 mm surfaces in the longitudinal direction. Width 5mm, thickness 1.0 along
The paste was arranged in a layer of mm. Next, Example 1
By sufficiently drying the paste under the same conditions as in the case of Example 1, a mixed powder layer 29 having a porosity of 40% was formed on the test piece 30, as shown in FIG. Next, as shown in FIG. 11, while emitting argon from the tip of the laser gun 31, the laser gun is scanned in one pass from one end to the other end of the mixed powder 29 to mix the powder under the conditions shown in Table 6 below. By irradiating the powder layer with a laser 32 to locally heat and melt the mixed powder layer, an alloy layer 33 made of an iron alloy in which titanium particles and tungsten particles were dispersed was formed. In this case, the formed alloy layer and the heated surface portion of the test piece were rapidly cooled mainly due to heat absorption by the main part of the test piece. Table 6 Power density: 320W/mm ^2Energy density: 220J/mm ^2Scanning speed: 4.0mm/sec Argon flow rate: 10/min Next, as in Example 2, the test piece was placed on the mounting table inside the reaction vessel. By introducing a mixed gas of carbon monoxide, carbon dioxide, and nitrogen (mixing ratio 2:3:5) into the reaction vessel while exhausting the air inside the reaction vessel, the inside of the reaction vessel becomes a carbonizing gas. The inside of the reaction container was heated to 1300°C for 8 hours using a heater placed around the reaction container, thereby causing the reaction 2CO+CO ₂ →C+2CO ₂ Ti+C→TiC W+C→WC to occur in the alloy layer. By carbonizing the titanium particles and tungsten particles, a composite layer made of an iron alloy in which titanium carbide particles and tungsten carbide particles were dispersed was formed. The composite layer formed as described above had a width of 6.0 mm and a maximum thickness of 1.8 mm. Furthermore, when we observed the cross section of the central part of the test piece, we found that, as in Examples 1 and 2, there was a heat-affected zone between the composite layer and the base metal of the test piece. The width was about 0.8 to 1.0 mm. Furthermore, the total volume fraction of titanium carbide particles and tungsten carbide particles in the composite layer is approximately 10%, and the dispersion state of these particles is substantially uniform throughout the composite layer. It was also observed that the adhesion between the composite layer and the iron alloy as the matrix metal and the integrity of the composite layer and the test piece were good. Furthermore, the average particle diameter of titanium carbide particles and the average particle diameter of tungsten carbide particles were both 2 μ. FIG. 12 is an optical micrograph showing the metal structure at the center of the longitudinal cross-section of the composite layer at 400 times magnification. In the figure, the light gray parts are iron alloy parts as the matrix metal, and the fine black granular parts are titanium carbide or tungsten carbide particles. From FIG. 14, it can be seen that very fine and uniformly sized titanium carbide particles and tungsten carbide particles are uniformly dispersed in the matrix metal, and defects such as pores are not generated at all. Although the present invention has been described in detail with respect to specific embodiments above, the present invention is not limited to these embodiments, and various embodiments are possible within the scope of the present invention. will be clear to those skilled in the art.

[Brief explanation of drawings]

Figure 1 is a perspective view showing how to place the paste on the surface of a test piece, with parts of the paste and guide cut away; Figure 2 is a perspective view showing a test piece with a chromium powder layer formed on the surface; Figure 3 is an illustration showing the process of melting the chromium powder layer on the test piece using a TIG arc to form an alloy layer. A cross-sectional view showing the process of oxidizing chromium particles, FIG. 5 is an illustrative cross-sectional view showing a longitudinal cross-section of the central part of the test piece on which a composite layer has been formed, and FIG. An optical micrograph showing the metal structure at the center of the cross section of a composite layer made of iron alloy at 800x magnification, Figure 7 shows an alloy layer formed by melting a titanium powder layer with a laser in an inert atmosphere. An illustration showing the process, Figure 8 is a cross-sectional view showing the process of nitriding the titanium particles in the alloy layer formed by the process in Figure 7, and Figure 9 is a composite made of iron alloy in which titanium nitride particles are dispersed. Optical micrograph showing the metal structure in the center of the cross section of the layer at 800x magnification.
FIG. 10 is a perspective view showing a test piece with a mixed powder layer formed on its surface; FIG. 11 is an illustrative diagram showing the process of melting the mixed powder layer with a laser in an inert atmosphere to form an alloy layer; Figure 12 shows the metal structure in the center of the cross section of a composite layer made of an iron alloy in which titanium carbide particles and tungsten carbide particles are dispersed.
This is an optical microscope photograph shown at 400x magnification. 1... Test piece, 2, 3... Guide, 4... Paste, 5... Chrome powder layer, 6... TIG torch,
7... TIG arc, 8... Alloy layer, 9... Reaction vessel, 10... Mounting table, 11... Mixed powder, 12...
... Heater, 13 ... Chromium oxide particles, 14 ... Iron alloy, 15 ... Composite layer, 16 ... Base metal, 1
7... Heat affected zone, 18... Test piece, 19... Laser gun, 20... Powder supply hopper, 21... Titanium powder, 22... Titanium powder layer, 23...
... laser, 24 ... alloy layer, 25 ... reaction vessel,
26... Mounting table, 27... Heater, 28... Composite layer, 29... Mixed powder layer, 30... Test piece, 31
... Laser gun, 32 ... Laser, 33 ... Alloy layer.

Claims (1)

[Scope of Claims] 1. Powder of a metal element having higher reactivity with oxygen than the main constituent elements of the metal material is arranged on the surface of the metal material, and the powder and the surface layer of the metal material are exposed to a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer, comprising dispersing the highly reactive metal in the surface layer of the metal material by heating and melting the metal material, and heating the surface layer in an oxidizing gas atmosphere. 2. In the method for forming a ceramic particle-dispersed metal composite layer according to claim 1, the molten powder and the surface layer of the metal material are rapidly cooled mainly due to heat absorption by a portion of the metal material other than the surface layer. A method for forming a ceramic particle-dispersed metal composite layer. 3. In the method for forming a ceramic particle-dispersed metal composite layer according to claim 1 or 2, the powder and the surface layer of the metal material are heated and melted with a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer, characterized in that the step of dispersing a highly reactive metal in the surface layer of the metal material is carried out in an inert atmosphere. 4. The method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 1 to 3, wherein the high-density energy source is a TIG arc. How to form. 5. The method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 1 to 4, wherein the gas is a mixed gas of oxygen and an inert gas. Method for forming a dispersed metal composite layer. 6 Powder of a metal element that is more reactive with nitrogen than the main constituent elements of the metal material is placed on the surface of the metal material, and the powder and the surface layer of the metal material are heated and melted with a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer, comprising dispersing the highly reactive metal in the surface layer of the metal material and heating the surface layer in a nitriding gas atmosphere. 7. In the method for forming a ceramic particle-dispersed metal composite layer according to claim 6, the molten powder and the surface layer of the metal material are rapidly cooled mainly due to heat absorption by a portion of the metal material other than the surface layer. A method for forming a ceramic particle-dispersed metal composite layer. 8. In the method for forming a ceramic particle-dispersed metal composite layer according to claim 6 or 7, the powder and the surface layer of the metal material are heated and melted with a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer, characterized in that the step of dispersing a highly reactive metal in the surface layer of the metal material is carried out in an inert atmosphere. 9. The method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 6 to 8, wherein the high-density energy source is a laser. Formation method. 10. The method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 6 to 9, wherein the gas is a mixed gas of nitrogen and ammonia gas. Method of forming metal composite layer. 11 Powder of a metal element that is more reactive with carbon than the main constituent elements of the metal material is placed on the surface of the metal material, and the powder and the surface layer of the metal material are heated and melted with a high-density energy source. A method for forming a ceramic particle-dispersed metal composite layer, comprising dispersing the highly reactive metal in the surface layer of the metal material and heating the surface layer in a carbonizing gas atmosphere. 12 In the method for forming a ceramic particle-dispersed metal composite layer according to claim 11, the molten powder and the surface layer of the metal material are rapidly cooled mainly by heat absorption by a portion of the metal material other than the surface layer. A method for forming a ceramic particle-dispersed metal composite layer. 13 In the method for forming a ceramic particle-dispersed metal composite layer according to claim 11 or 12,
The process of dispersing the highly reactive metal into the surface layer of the metal material by heating and melting the powder and the surface layer of the metal material with a high-density energy source is performed in an inert atmosphere. A method for forming a ceramic particle-dispersed metal composite layer, characterized in that: 14. The method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 11 to 13, wherein the high-density energy source is a laser. Formation method. 15 In the method for forming a ceramic particle-dispersed metal composite layer according to any one of claims 11 to 14, it is provided that the gas is a mixed gas of carbon monoxide, carbon dioxide, and an inert gas. Characteristic method for forming a ceramic particle-dispersed metal composite layer.