JP3009527B2 - Aluminum material excellent in wear resistance and method for producing the same - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum material having excellent wear resistance and a method for producing the same, and more particularly, to an aluminum material having a surface layer having excellent wear resistance on the surface of an aluminum material and a method for producing the same. It is about.

[0002]

2. Description of the Related Art An aluminum material or an aluminum alloy material (hereinafter, referred to as an aluminum material) itself has poor abrasion resistance and seizure resistance, and thus has a problem in durability of a sliding surface of a moving part. Further, since the hardness of the base material is lower than that of steel, there is a disadvantage that it cannot withstand a high surface pressure.

[0003] As a method of solving these problems, there is a method of subjecting an aluminum material to plasma spraying or laser or the like to alloy the surface of the aluminum material, or a method of plating.

Further, prior to ion nitriding of the aluminum material, the surface of the material to be treated is activated by introducing an activating gas comprising a rare gas such as helium or argon and discharging the same. "Ion-nitriding method of aluminum material" to form an excellent aluminum nitride layer on the surface of the material to be treated by ion-nitriding to obtain a surface property in which a nitride layer is easily formed (JP-A-60-211061) Is being developed. According to this method, a coating layer having high hardness can be easily formed on the surface of aluminum, so that the wear resistance of the aluminum material can be improved. That is, the aluminum nitride layer formed on the surface of the aluminum material is stable up to a very high temperature, has a hardness of Hv 1000 or more, has excellent wear resistance, has high thermal conductivity, and has excellent insulation.

[0005]

However, since the former method is a method of melting metal, it has a problem that the thickness and composition of the surface layer are not uniform and the hardness and wear resistance characteristics are not uniform. ing. In addition, there is a problem that grinding or polishing after the treatment is required due to poor surface roughness. Further, when a thick composite plating layer is formed by a plating method such as electroplating, there is a problem that the adhesion between the base material and the base material is not sufficient because the base material and the interface are mechanically bonded.

Further, the ion nitriding method of aluminum material disclosed in Japanese Patent Application Laid-Open No. Sho 60-211061 is capable of forming a surface layer having high hardness and excellent abrasion resistance. The thickness is at most about 10 μm, and when used as a member to which a high surface pressure is applied, there is a problem that the member may not be able to withstand the pressure.

The inventors of the present invention have conducted intensive studies to solve the above-mentioned problems of the prior art, and have conducted various systematic experiments. As a result, the present invention has been accomplished.

(Object of the Invention) It is an object of the present invention to provide an aluminum material having excellent wear resistance and high hardness and excellent surface pressure strength characteristics, and a method for producing the same.

The present inventors have focused on the following with respect to the above-mentioned problems of the prior art. That is, attention was paid to providing a surface layer on the surface of the aluminum material, which has higher hardness than aluminum, has good sliding characteristics, has a coefficient of thermal expansion relatively close to that of aluminum, and is not damaged by external force.

In view of the above, as a layer satisfying the above conditions, a surface layer made of an Al-Ag intermetallic compound having a predetermined film thickness is provided by focusing on an intermetallic compound of silver and aluminum. The inventors have found that the problem can be solved, and have accomplished the present invention.

[0011]

Means for Solving the Problems (First Invention) The aluminum material having excellent wear resistance according to the first invention comprises a base material made of aluminum or an aluminum alloy material, and aluminum and silver formed on the surface of the base material. Ri of Do and a intermetallic compound layer, the thickness of the intermetallic compound layer 50μm~2
And wherein the 00μm der Rukoto.

(Second invention) The aluminum material having excellent wear resistance according to the second invention comprises a base material made of aluminum or an aluminum alloy material and an intermetallic compound of aluminum and silver formed on the surface of the base material. It is characterized by comprising an intermediate layer and an aluminum nitride layer formed on the surface of the intermediate layer.

(Third Invention) The method for producing an aluminum material having excellent wear resistance according to the third invention is a step of preparing a base material made of aluminum or an aluminum alloy material, and using silver as a main component on the surface of the base material. Forming a metal layer and heat-treating the aluminum base material coated with the metal layer to diffuse aluminum into the metal layer to form an aluminum-silver intermetallic compound layer having a thickness of 50 μm to 200 μm. characterized by comprising a diffusion process Toka et.

(Fourth Invention) The method for producing an aluminum material having excellent wear resistance according to the fourth invention comprises the steps of: preparing a base material made of aluminum or an aluminum alloy material; The method is characterized by a step of forming an intermediate layer made of an intermetallic compound, and a step of subjecting the intermediate layer to a nitriding treatment to form an aluminum nitride layer on the surface of the layer.

[0015]

The mechanism by which the method of manufacturing the aluminum material having excellent wear resistance according to the first or second invention and the method of manufacturing the aluminum material having excellent wear resistance according to the third and fourth inventions exhibit excellent effects. Is not necessarily clear yet, but is considered as follows.

(Operation of the First Invention) The aluminum material of the present invention comprises a base material made of aluminum or an aluminum alloy material, and an intermetallic compound layer formed on the surface of the base material. This intermetallic compound layer is an intermetallic compound of aluminum and silver. The intermetallic compound composed of silver and aluminum has a coefficient of thermal expansion relatively close to that of the base material, and has a higher hardness than aluminum. By using this intermetallic compound of silver and aluminum, the interface with the aluminum base material becomes a metal bond due to diffusion, and the difference in thermal expansion coefficient is small, so that the shear force at the interface with respect to temperature change is small, It is considered that the resulting aluminum material has excellent adhesion to the layer, has excellent wear resistance, and has higher hardness and a certain degree of toughness than the aluminum base material.

The surface of the aluminum material is made of Cu or N
i, coated with other metal such as Cu-Al
Alternatively, it is conceivable to form an intermetallic compound composed of Ni-Al.
Has a problem that the thermal expansion coefficient is smaller than that of the aluminum base material, and the intermetallic compound lacks toughness and is easily peeled. In the case of the present invention, a unique effect that such a problem hardly occurs can be obtained.

(Operation of the Second Invention) The aluminum material of the present invention comprises a base material made of aluminum or an aluminum alloy material, an intermediate layer made of an intermetallic compound layer of aluminum and silver formed on the surface of the base material, And an aluminum nitride layer formed on the surface of the intermediate layer. The aluminum nitride layer as a surface layer is stable up to a very high temperature, has a hardness of Hv 1000 or more, has excellent wear resistance, has high thermal conductivity, and has excellent insulation. The aluminum material of the present invention has an intermetallic compound consisting of aluminum and silver between the aluminum nitride surface layer and the base material.
This intermetallic compound has a higher hardness than the base material, has toughness, and has a predetermined film thickness. Therefore, the aluminum material of the present invention can exhibit the characteristics of the aluminum nitride layer as the surface layer as it is, and even when a considerable surface pressure is applied to the surface of the material, the surface pressure is reduced by the intermediate layer. Therefore, it is considered that the effect of the surface layer can be exerted, and deformation that impairs the predetermined effect can be prevented.

(Operation of the Third Invention) In the method for producing an aluminum material having excellent wear resistance according to the third invention, first, a base material made of aluminum or an aluminum alloy material is prepared (base material preparation step). Next, a metal layer mainly composed of silver is formed on the surface of the wear-resistant layer forming portion of the base material by an electroplating method or the like (silver layer forming step). Next, the aluminum base material coated with the metal layer is heat-treated, and aluminum is diffused into the metal layer to form an intermetallic compound layer of aluminum and silver (thermal diffusion processing step). At this time, silver easily reacts with aluminum and has a high diffusion rate, so that Ag can be easily formed.
It is believed that it is possible to form an intermetallic compound consisting of ₂ Al. Further, the obtained intermetallic compound of aluminum and silver has excellent wear resistance, relatively high hardness, and excellent surface pressure strength characteristics.

(Operation of the Fourth Invention) In the method for manufacturing an aluminum material having excellent wear resistance according to the fourth invention, a base material made of aluminum or an aluminum alloy material is prepared (base material preparation step). Next, an intermediate layer made of an intermetallic compound of aluminum and silver is formed on the surface of the base material (intermediate layer forming step). The formation of the intermediate layer can be performed in the same manner as in the third invention. Next, nitriding is performed by a method such as an ion nitriding method or a nitriding bath immersion method to form an aluminum nitride layer on the surface of the intermediate layer (an aluminum nitride layer forming step). As a result, aluminum constituting the intermediate layer diffuses to the surface, and the aluminum and nitrogen combine to form an aluminum nitride layer. At this time, the aluminum component of the intermediate layer, which has been lost due to the formation of the aluminum nitride layer, is rapidly supplemented from the base material since the diffusion speed of aluminum into silver is high, so that a relatively thick aluminum nitride layer can be formed. Thus, a base material, an intermediate layer made of an intermetallic compound of aluminum and silver, and a surface layer made of aluminum nitride have abrasion resistance and hardness,
Further, it is considered that an aluminum material having a three-layer structure having excellent surface pressure strength can be easily obtained.

[0021]

【The invention's effect】

(Effect of the First Invention) The aluminum material of the first invention has excellent abrasion resistance, has higher hardness and toughness than the base metal, and has excellent surface pressure strength characteristics.

(Effect of the Second Invention) The aluminum material of the second invention has more excellent wear resistance and higher hardness, and also has excellent surface pressure strength characteristics.

(Effect of the Third Invention) According to the manufacturing method of the third invention, the surface of aluminum or aluminum alloy as a base material (material to be treated) has excellent wear resistance, high hardness, and surface pressure strength. An intermetallic compound layer having excellent characteristics can be easily formed. Further, the intermetallic compound layer formed on the surface of the base material has excellent adhesion.

(Effect of the Fourth Invention) According to the manufacturing method of the fourth invention, the surface of aluminum or an aluminum alloy as a base material (material to be treated) has higher abrasion resistance and higher hardness, A coating layer having excellent pressure strength characteristics can be easily formed. Further, the coating layer formed on the surface of the base material has excellent adhesion.

[0026]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS First, a description will be given of an invention (a specific example) in which the method of manufacturing the aluminum material of the first or second invention and the aluminum material of the third or fourth invention are more concretely described.

The base material or the material to be processed according to the present invention is a material or a member made of aluminum or an aluminum alloy. It may be in the form of a product before surface treatment. The aluminum alloy contains aluminum as a main component and contains one or more of silicon, copper, magnesium, manganese, chromium, nickel, iron, zinc, and the like.

Layer composed of an intermetallic compound of aluminum and silver (intermetallic compound layer as surface layer or intermediate layer)
Is a layer for improving the wear resistance, hardness and surface pressure strength of the base material, and is specifically made of Ag ₂ Al or the like. Further, Ag-Ag ₂ Al (silver-rich intermetallic compound) or Al-Ag ₂ Al (aluminum-rich intermetallic compound) may be used. The properties such as the Al content in the layer, the thickness of the layer, and the hardness of the layer can be appropriately determined according to the purpose.

When the intermetallic compound layer is used as a surface layer, the thickness is preferably 50 μm to 200 μm. If the film thickness is less than 50 μm, depending on the application, it may be plastically deformed by surface pressure and the surface shape may be changed, and if the film thickness exceeds 200 μm, the layer forming process time becomes longer, There is a possibility that the amount of silver used will increase and the cost will increase. Also, when used as an intermediate layer, the film thickness is 50 μm to 2 μm for the same reason as described above.
It is preferably 00 μm.

The hardness of the intermetallic compound, when formed of pure aluminum and pure Ag, is about Hv 200 to 2
50, which is about Hv 80 of a practical aluminum alloy.
Higher than ~ 140. Therefore, for applications where a conventional aluminum alloy is used and the surface pressure resistance is insufficient, the coating of the aluminum base material surface with the intermetallic compound is effective. However, even for about Hv 200 to 250, for applications in which the surface layer is deformed, an intermetallic compound layer of Hv 300 or more is formed by adding another element to Ag to reduce the Hv to about 700. It is also possible.

Further, a third element can be appropriately added to the intermetallic compound layer as long as the effect of the present invention is not impaired. For example, if higher hardness is desired, chromium (Cr), copper (Cu), iron (Fe), nickel (N
It is preferable to add at least one kind of property improving element such as i).

The method of forming the intermetallic compound on the surface of the base material includes electroplating, electroless plating, thermal spraying,
A paste coating method or the like can be applied. In addition, according to the above method, first, a metal film mainly composed of silver is formed, and a base material having the metal film is heated to diffuse aluminum in the base material into the metal film and to be formed of aluminum and silver. Intermetallic compounds can be formed.

The base material made of an aluminum material is
Since an oxide film is easily formed on the surface, a metal film mainly composed of silver is first formed by electroplating, and then the base material coated with the metal film is heated to diffuse aluminum in the base material into the metal film. It is preferable to form an intermetallic compound composed of aluminum and silver on the surface of the base material by performing the treatment. Employing the electroplating method is preferable because it can cover only a portion requiring a uniform layer. In addition, this method has the advantage that even small parts can be processed simultaneously, and is suitable for mass coating.

When the intermetallic compound layer is formed as an intermediate layer, the thermal diffusion treatment in the intermetallic compound forming step (intermediate layer forming step) is performed simultaneously with the heat treatment in the subsequent nitriding step. Is also good. For example, in the case where the nitriding treatment is performed by an ion nitriding treatment method, it can also serve as a step involving heat application of the material to be treated, such as a temperature raising step in the ion nitriding treatment. In this case, there is an advantage that the process can be simplified and the cost can be reduced.

The aluminum nitride layer is a surface layer formed on the surface of the intermetallic compound layer (intermediate layer), is stable up to a very high temperature, has a hardness of Hv 1000 or more, has excellent wear resistance, and has excellent thermal conductivity. This layer is large and has excellent insulating properties. The aluminum nitride layer may contain a property improver composed of at least one of oxygen, nitrogen, carbon and the like for the purpose of improving the properties of the layer, as long as the effect of the invention is not impaired. For example, in the case of an aluminum oxynitride layer having an oxygen content of 1 to several tens% by weight, the layer can be further excellent in water resistance and corrosion resistance.

This aluminum nitride layer has a thickness of 2 μm.
It is preferably from 10 to 10 μm. If the film thickness is less than 2 μm, it may not be possible to provide more excellent and sufficient wear resistance. If the film thickness exceeds 10 μm, substances such as cracks which impair the wear resistance may be present. There is a possibility that the rate of the operation may be increased.

As a method for forming the aluminum nitride layer, various chemical vapor deposition methods such as an ion nitriding method and a plasma chemical vapor deposition method, various physical vapor deposition methods such as an ion plating method, and a salt containing cyanide are used. Any method such as various immersion methods such as a method of immersion in a bath can be applied.

The aluminum nitride layer is formed by preferentially nitriding aluminum in the intermediate layer formed of the intermetallic compound formed on the base material, and bonding the aluminum with nitrogen supplied from the outside. It is preferable to use a method in which aluminum nitride is formed. According to this method, aluminum is an element diffused from Ag ₂ Al and reacts with nitrogen on the surface to form AlN. Therefore, aluminum can have excellent adhesion strength between the intermediate layer and the aluminum nitride layer. . Ag and N are not considered to be bonded from the conventional thermodynamic data, and are not formed in the present invention.

Here, an example of a method of forming an aluminum nitride layer will be briefly described as follows. That is, as a method of forming the aluminum nitride layer by an ion nitriding method, first, a material in which an intermediate layer made of an intermetallic compound of aluminum and silver is formed in a base material, or a metal in which a base material is mainly silver A material on which a film is formed is prepared and placed in a nitriding apparatus (material placement step). Next, after the container is sealed, gas remaining in the container is removed using a vacuum pump such as a rotary pump or a diffusion pump (oxygen gas removing step). Note that, if necessary, the introduced gas composed of a non-oxidizing gas such as a hydrogen gas or a rare gas is replaced after the pressure reduction, and the pressure reduction is repeated. Then
Either a gas for raising the temperature is introduced into the depressurized closed vessel and discharge is performed, or the surface of the material to be treated is heated to a predetermined nitriding temperature by a heater provided in or around the vessel (raise). Temperature process). In the case where the prepared material is the latter, that is, when the metal film formed on the surface of the base material is a metal film mainly composed of silver instead of the intermetallic compound, the heat treatment in this temperature raising step Then, aluminum in the base material is diffused into the metal film to form an intermetallic compound. Next, a nitriding gas such as a nitrogen gas, a gas mainly containing nitrogen, or a mixed gas of a nitrogen gas and a hydrogen gas is introduced into the closed container, and a glow discharge is generated in the closed container to perform processing. A nitriding treatment is performed on the material surface (ion nitriding step). Note that, prior to the ion nitriding treatment, the surface of the material to be treated is preferably subjected to a pretreatment so that aluminum nitride is easily formed, so that a thick aluminum nitride layer can be formed efficiently and preferably.

When an ion nitriding method is applied as a method for forming an aluminum nitride layer, the method is performed in a gas, so that there is an advantage that post-cleaning is unnecessary and simultaneous processing is possible.

In the case of the ion nitriding method, it is preferable to perform the nitriding treatment so that the temperature of the material to be treated is as uniform as possible. For example, the condition of glow discharge is
It is preferable to consider the holding and electrodes of the components so that the discharge is uniformly generated in each part or each component.

An example of a method of forming the aluminum nitride layer by an immersion method will be briefly described. That is, it is usually immersed in a bath containing cyan used for the salt bath nitriding of steel.

When the immersion method is applied as the method for forming the aluminum nitride layer, since it is a salt bath, there is an advantage that the temperature can be easily controlled.

Here, an example of the structure of the aluminum material of this example will be described with reference to FIG. That is, FIG.
A cross section of an aluminum material is schematically shown. A base material (forged material or cast material: A7075: maximum Hv 150) 1 made of aluminum or aluminum alloy;
Intermediate layer (backup layer: 50) formed on the surface of the base material
200 μm: Hv 300 to 600) 2 and an aluminum nitride layer (wear layer: 2 to 10 μm) formed on the surface of the intermediate layer.
m: Hv 1000-2000) 3.

An embodiment of the present invention will be described below.

First Embodiment

Using pure Al as a base material, a metal film made of silver was formed by electrolytic plating, and a heat diffusion treatment was performed to produce an aluminum material, and a performance evaluation test of the material was performed.

First, pure aluminum (manufactured by A1100) having a size of 50 × 25 × 5 mm was prepared as a base material. Next, about 45 μm and about 80 μm were formed on the surface of the base material by electrolytic plating.
A silver (Ag) plating layer having a thickness of m was formed. Next, the sample on which these silver plating layers are formed is placed in a vacuum (about 10 ^-3 to 1
The diffusion treatment was carried out at 450 ° C., 500 ° C., 540 ° C. and 570 ° C., which is almost the eutectic temperature (567 ° C.), for 1, 2, or 4 hours at 0 ^-4 Torr.

The performance of the obtained aluminum material was evaluated by X-ray diffraction, optical microscope observation, hardness measurement, and element distribution measurement by EPMA.

First, the X-ray diffraction test was performed by irradiating X-rays from the surface of the sample after heating. as a result,
In all samples, the coating film formed on the base material surface was Ag ₂ Al
It was found to be an intermetallic compound consisting of

Next, an optical microscope observation test was performed on a surface obtained by cutting a sample obtained after heating, embedding the sample in a resin, and then polishing the sample. As a result, none of the problems such as cracks and peeling were observed at all, and it was found that the coating film was formed uniformly. FIG. 2 shows the metal structure (magnification: 200 times) of the cross section of the aluminum material in the case where the heating temperature in the heat diffusion treatment is 540 ° C. and the heating time is 4 hours.

FIG. 3 shows the relationship between the heating temperature and the thickness of the coating layer. As can be seen from the figure, the higher the heating temperature and the longer the heating time, the thicker the coating layer.

Next, the hardness measurement test was performed with a load of 100 g using a micro-Vickers hardness tester. As a result, the hardness distribution of the Ag ₂ Al intermetallic compound is Hv 210 to 2
It was found that it was 30 and was irrelevant to the type of the base material and the processing conditions. In addition, no crack was generated due to the indentation in the hardness measurement of the layer.

Next, the element distribution measurement test by EPMA was performed using the same sample as the sample in the optical microscope observation test. FIG. 4 shows the measurement results of an example in which the heating temperature in the heat diffusion treatment was 540 ° C. and the heating time was 4 hours. As is clear from the figure, Ag is about 80% by weight and Al is about 15% by weight inside the coating layer, and this composition is within the solid solution range of Ag ₂ Al shown in the equilibrium diagram.
This corresponds to the l-rich Ag ₂ Al portion.

For comparison, a metal film was formed on the base material in the same manner as in the first embodiment, except that the metal film formed on the surface of the base material was changed to about 20 μm Cu or Ni instead of Ag of the above-described embodiment. Was formed and subjected to heat diffusion treatment to prepare an aluminum material for comparison, and a performance evaluation test was performed. As a result, cracks were generated in the cross-sectional structures when the Cu and Ni plated materials were heated, and the plated layer was sometimes peeled off during cooling. Also, Ag ₂ in the Ag plating material
It was found that the growth rate coefficient K of the Al layer was 120 to 250 times that of the Cu and Ni plating materials.

From this example, it was also found that since the growth rate of the Ag ₂ Al layer was extremely high, a thick layer could be formed on the surface of the aluminum material in a short time.

Second Embodiment

Using duralumin as a base material,
In the same manner as in the example, a metal film made of silver was formed by electrolytic plating, and a heat diffusion treatment was performed to produce an aluminum material, and a performance evaluation test of the material was performed.

First, duralumin (manufactured by A 2017) having a size of 50 × 25 × 5 mm was prepared as a base material. Next, a silver plating layer is formed in the same manner as in the first embodiment,
Diffusion treatment was performed to obtain an aluminum material according to the present example.

The performance of the obtained aluminum material was evaluated in the same manner as in the first embodiment by X-ray diffraction, observation with an optical microscope, hardness measurement, and element distribution measurement by EPMA.

As a result, the X-ray diffraction test revealed that the coating film formed on the surface of the base material was an intermetallic compound composed of Ag ₂ Al in all samples. The optical microscopic structure of the cross section of the obtained aluminum material was the same as that of the pure aluminum of the first example, and a metal coating layer without cracks or peeling was formed. Moreover, the hardness distribution of the Ag ₂ Al intermetallic compound is Hv 210 ~ 230, moreover, been found to be independent of the type and processing conditions of the base material. In addition, no crack was generated due to the indentation in the hardness measurement of the layer. The analysis result by EPMA shows that the heating temperature in the heating diffusion process is 540 ° C. and the heating time is 4 hours.
FIG. 5 shows the results measured for the example of time. As is clear from the figure, the distribution of Ag and Al inside the coating layer is the same as in the case of A 1100 in the first embodiment, but Cu, which is an alloy element in the base material, is the largest in the coating layer. Mn and S were present at about 1.5% by weight and up to about 0.5% by weight Mg.
The presence of i was not confirmed.

Third Embodiment

Using pure Al and duralumin as a base material, a metal film made of Ag + Ni was formed by composite electrolytic plating, and a heat diffusion treatment was performed to produce an aluminum material, and a performance evaluation test of the material was performed.

First, as a base material, pure aluminum (manufactured by A1100) having a size of 50 × 25 × 5 mm and duralumin (A
2017). Then, a composite plating layer of silver-nickel (Ag + 5% Ni) having a thickness of about 45 μm and about 80 μm was formed on the surface of the base material by composite electrolytic plating. Next, the samples on which the plating layers are formed are subjected to vacuum (about 10 ⁻³ to 10 ⁻⁴ Torr) in the same manner as in the first embodiment.
The diffusion treatment was performed by heating at 450 ° C., 500 ° C., 540 ° C. and 570 ° C., which is almost the eutectic temperature (567 ° C.), for 1, 2, or 4 hours.

The performance of the obtained aluminum material was evaluated in the same manner as in the first embodiment by X-ray diffraction, observation with an optical microscope, hardness measurement, and element distribution measurement by EPMA.

As a result, the X-ray diffraction test revealed that the coating film formed on the base material surface was an intermetallic compound containing Ag ₂ Al as a main component in all samples. The optical microscopic structure of the cross section of the obtained aluminum material was the same as that of the pure aluminum of the first example, and a metal coating layer without cracks or peeling was formed. Ag ₂
The hardness distribution of the Al intermetallic compound is Hv 450 to 510,
In addition, it was found that it was irrelevant to the type of the base material and the processing conditions. In addition, no crack was generated due to the indentation in the hardness measurement of the layer.

Similarly, when Cr or Fe was used instead of Ni in the composite plating layer, the effect of increasing the hardness of the coating layer was recognized as in the third embodiment.

Fourth Embodiment

The Ag-Al intermetallic compound layers prepared in the first and second embodiments are coated with an aluminum material, and the surface of the coating layer is ion-nitrided to form an aluminum nitride layer. The aluminum material according to the second invention was produced. Next, performance evaluation test results of the aluminum material were performed.

First, Ag-Al intermetallic compound layers prepared according to the first and second embodiments were prepared and placed in an ion nitriding apparatus. Next, after the container was sealed, the gas remaining in the container was removed using a rotary pump, and then the hydrogen gas was replaced by introduction, and the pressure was repeatedly reduced. Next, hydrogen gas was introduced as a heating gas into the depressurized closed vessel, and discharge was performed. The surface of the material to be treated was heated to 500 ° C. Next, 3 T in a closed container
orr nitrogen gas and 6
Glow discharge was generated under the conditions of 00 V and 1 A, and the surface of the workpiece was subjected to nitriding for 4 hours. As a result, a black layer was formed on the surface.

The black layer was subjected to a substance identification test by an X-ray diffraction method. As a result, it was confirmed that each of the black layers was a wurtzite type aluminum nitride (AlN).

Further, a measurement test of the film thickness of the nitride layer was performed for an example in which the heating temperature in the heating diffusion treatment was 500 ° C. and the heating time was 4 hours. As a result, the film thickness was about 8 μm. FIG. 6 shows the result of the structure observation by the optical microscope of the example, that is, the metal structure (magnification: 400 times) of the cross section of the aluminum material. As is clear from the figure,
The aluminum material according to the present embodiment includes a base material, an intermediate layer formed on the surface of the base material, and an aluminum nitride layer formed on the surface of the intermediate layer. Was not observed at all, indicating that the coating film was formed uniformly. In addition, EPMA of the surface layer of the example
FIG. 7 shows the results of the analysis. As is clear from the figure, Al and N were present in the surface layer. The hardness of the layer was Hv1500.

Fifth Embodiment

The Ag-Al intermetallic compound layer produced in the first and second embodiments is coated with an aluminum material, and the surface of the coating layer is nitrided by a molten salt immersion method to form an aluminum nitride layer. Then, an aluminum material according to the second invention of the present invention was produced. Next, performance evaluation test results of the aluminum material were performed.

First, an Ag-Al intermetallic compound layer prepared according to the first and second embodiments was prepared, and immersed in a salt bath containing cyanide for 4 hours to be nitrided.

A material identification test was performed on the surface layer of this sample by an X-ray diffraction method, and as a result, it was confirmed that all were aluminum nitride (AlN).

Further, a measurement test of the film thickness of the nitride layer was performed on an example in which the heating temperature in the heating diffusion treatment was 500 ° C. and the heating time was 4 hours. As a result, the film thickness is about 10 μm
Met.

[Brief description of the drawings]

FIG. 1 is an explanatory view schematically showing a cross-sectional structure of a specific example of the aluminum material of the second invention.

FIG. 2 is an optical micrograph showing a metal structure of a cross section of the aluminum material obtained according to the first embodiment of the present invention (magnification:
200 times).

FIG. 3 is a diagram showing the relationship between the heating temperature (diffusion processing temperature) of the aluminum material obtained according to the first embodiment of the present invention and the thickness of the coating layer.

FIG. 4 is a diagram showing a test result of element distribution measurement by EPMA of the aluminum material obtained according to the first embodiment of the present invention.

FIG. 5 is a diagram showing a test result of element distribution measurement of an aluminum material obtained by a second embodiment of the present invention by EPMA.

FIG. 6 is an optical micrograph showing a metal structure of a cross section of an aluminum material obtained according to a fourth embodiment of the present invention (magnification:
400 times).

FIG. 7 is a diagram showing a test result of element distribution measurement by EPMA of an aluminum material obtained according to a fourth embodiment of the present invention.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 ... Base material 2 ... Intermediate layer 3 ... Aluminum nitride layer

Claims (4)

(57) [Claims] 1. A and the base material made of aluminum or an aluminum alloy material, Ri Do from the intermetallic compound layer of aluminum and silver formed on the base material surface, the intermetallic compound layer
Aluminum product thickness of excellent wear resistance, wherein 50μm~200μm der Rukoto. 2. A base material made of aluminum or an aluminum alloy material, an intermediate layer made of an intermetallic compound of aluminum and silver formed on the surface of the base material, and an aluminum nitride layer formed on the surface of the intermediate layer. Aluminum material with excellent wear resistance. 3. A step of preparing a base material made of aluminum or an aluminum alloy material, a step of forming a metal layer mainly composed of silver on the surface of the base material, and heat-treating the aluminum base material coated with the metal layer. The aluminum is diffused into the metal layer to have a thickness of 50 μm or more.
Method for producing a wear-resistant excellent aluminum material, characterized by comprising thermal diffusion treatment step Toka et of intermetallic compound layer with 200μm aluminum and silver. 4. A step of preparing a base material made of aluminum or an aluminum alloy material, a step of forming an intermediate layer made of an intermetallic compound of aluminum and silver on the surface of the base material, and performing a nitriding treatment on the intermediate layer. And forming an aluminum nitride layer on the surface of the layer by a method for producing an aluminum material having excellent wear resistance.