JP2010007102A - Method for producing aluminum member, and surface nitriding device for aluminum material - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To stably produce an aluminum member having satisfactory wear resistance. <P>SOLUTION: An Al-Mg/Al<SB>2</SB>O<SB>3</SB>filler powder comprising alumina(Al<SB>2</SB>O<SB>3</SB>) powder and Al-Mg alloy powder and a base material composed of aluminum are mixed within a barrel vessel 1 in the presence of a treatment gas including a nitrogen gas, and a nitride layer is formed on the surface of the base material 3. In this case, it is preferable that, to the filler powder, the Al-Mg alloy powder is comprised in a blending ratio of 0.7 to 2.0 mass%. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to an aluminum member manufacturing method and an aluminum material surface nitriding apparatus, and more particularly to an aluminum member manufacturing method and an aluminum material surface nitriding apparatus with improved surface wear resistance.

Currently, aluminum alloys are used in many product fields because they have various characteristics such as lightness, recyclability, and high corrosion resistance.
In recent years, aluminum alloys have been attracting particular attention as structural materials in order to reduce the weight of transportation equipment such as automobiles, railway vehicles, ships, and aircraft that consume large amounts of energy and various industrial equipment from the viewpoint of energy saving. is there.

  However, an aluminum alloy as such a structural material is inferior in wear resistance when compared with a steel material, and has a great obstacle especially when used as a sliding part such as an engine part of an automobile. For this reason, improvement in the wear resistance of aluminum alloys is strongly demanded by various industries.

  Therefore, attention is paid to the high thermal conductivity, low thermal expansion, and high hardness (high wear resistance) of aluminum nitride (AlN), and an aluminum member having an aluminum nitride layer on the surface is being used as a structural material.

  In order to increase the hardness and wear resistance of the surface of an aluminum material, as a method of efficiently forming an aluminum nitride layer on the surface, conventionally, an ion nitriding method using a diffusion penetration phenomenon of nitrogen ions, Al- A powder coating method is known in which an Mg alloy powder is coated on a substrate surface and then heated in a nitrogen atmosphere. However, in the ion nitriding method, the growth rate of the nitride layer is slow, and it is difficult to obtain an aluminum nitride layer having a sufficient thickness on the surface of the substrate, and it is necessary to remove the oxide film by sputtering before the nitriding treatment. Since the hardness and the coefficient of thermal expansion between the physical layer and the substrate are different, there are problems that cracks occur and the surface is easily peeled off. In the powder coating method, the Al—Mg alloy powder applied to the base material is sintered on the surface of the base material, and the part shape is likely to change.

  On the other hand, a packed powder composed of alumina particles and Al-Mg alloy powder is filled in a fluidized bed furnace, fluidized by introducing nitrogen gas into the fluidized bed furnace, and aluminum or an aluminum alloy base in the fluidized bed. A surface nitriding method of an aluminum material has been developed that forms a nitride layer on the surface of a base material with high productivity by charging the material and treating it at a temperature lower than the melting point of the base material (see Patent Document 1).

According to this surface nitriding method, the growth rate of the nitride layer is improved, and further, a predetermined amount of argon gas is mixed into the nitrogen gas, and the furnace temperature is adjusted to prevent sintering of the Al-Mg alloy powder. It is said that.
JP 2000-160319 A

  However, according to the surface nitriding method, it is necessary to introduce nitrogen gas into a fluidized bed furnace and fluidize the filling powder only by jetting the gas when nitriding the surface of the base material. In some cases, the nitriding treatment becomes inefficient and it is difficult to stably obtain a nitride layer for imparting wear resistance to the aluminum material.

  The present invention has been made to solve the above-mentioned problems, and an object of the present invention is to provide an aluminum member manufacturing method and an aluminum material surface nitriding apparatus in which an aluminum member having good wear resistance can be stably obtained. It is to provide.

  In order to solve the above problems, a method for producing an aluminum member according to the present invention is a method for producing an aluminum member having an improved wear resistance by forming a nitride layer on the surface of an aluminum material. In the presence of a processing gas containing, a filler powder containing alumina powder or alumina particles and a base material made of aluminum or an aluminum alloy are mixed in a rotating or swinging barrel container, and nitride is formed on the surface of the base material The gist is to include a surface nitriding step for forming a layer.

Moreover, in the manufacturing method of the aluminum member of this invention, it is preferable that the said barrel container is rocking | fluctuating and is formed in polygonal column shape.
Moreover, in the manufacturing method of the aluminum member of this invention, it is preferable that Al-Mg alloy powder is contained with the mixture ratio of 0.7 mass% or more and 2.0 mass% or less with respect to the said filling powder.

In the method for producing an aluminum member of the present invention, in the surface nitriding step, it is preferable to form a nitride layer on the surface of the substrate at a treatment temperature of 610 ° C. or more and 640 ° C. or less.
In the method for producing an aluminum member of the present invention, it is preferable that in the surface nitriding step, a nitride layer is formed on the surface of the substrate with a treatment time of 3.4 hours to 7 hours.

  Furthermore, an aluminum material surface nitriding device according to the present invention is an aluminum material surface nitriding device for forming a nitride layer on the surface of the aluminum material and improving the wear resistance of the surface of the aluminum material, wherein A barrel container in which a powder or powder containing alumina particles and a base material made of aluminum or an aluminum alloy are accommodated, a processing gas introduction means for introducing a processing gas containing nitrogen gas into the barrel container, and the inside of the barrel container And a barrel container swinging means for swinging the barrel container at a predetermined angle while introducing the processing gas.

  According to the present invention, an aluminum member having good wear resistance can be obtained stably.

  In the method for producing an aluminum member of the present invention, in the presence of a processing gas containing nitrogen gas, the inside of a barrel container that rotates or swings a filling powder containing alumina powder or alumina particles and a base material made of aluminum or an aluminum alloy is rotated. And a surface nitriding step of forming a nitride layer on the surface of the substrate. Thus, the base material (aluminum material) to be nitrided is efficiently stirred with the filling powder containing aluminum in the presence of nitrogen gas in a barrel container in which the base material (aluminum material) rotates or swings. Then, the base material reacts with nitrogen gas, and a nitride layer is formed on the surface of the base material. As a result, even if the base material exhibits a complicated surface shape, an aluminum member having high hardness and excellent wear resistance can be stably produced.

  The base material is a block (lumped) made of aluminum (Al) or an aluminum alloy. Here, as the aluminum alloy, for example, aluminum containing copper, manganese, zinc, silicon, magnesium, and the like, and various properties can be used, and a heat treatment type alloy is included.

  Such pure aluminum (pure aluminum) or an aluminum alloy is usually covered with an oxide film and is excellent in anticorrosion, but the reaction with nitrogen is inhibited by this oxide film. For this reason, in order to form a nitride layer on the substrate surface, it is necessary to activate the substrate surface.

As shown in FIG. 1 (a), in the nitriding method according to the present invention, a barrel container 1 (barrel tank) used for plating and polishing is used. The barrel container 1 is rotated or swung around the point O, and the collision between the filling powder 2 and the base material 3 is caused in the barrel container 1 by the rotation or swinging motion (filling powder). A part of 2 forms a collapsing layer 2a in the upper layer). By this collision, the substrate surface is physically activated, and a high hardness and high wear resistance nitride layer (AlN layer) can be formed on the substrate surface. Note that the nitride layer is not necessarily composed of only aluminum nitride, and usually includes unreacted aluminum, alumina (Al ₂ O ₃ ), magnesium, and the like.

As the filling powder 2, one containing alumina powder or alumina particles is used. Specifically, a mixture (Al-Mg / Al ₂ O ₃ filled powder) of alumina powder (Al ₂ O ₃ powder) and aluminum-magnesium alloy powder (Al-Mg alloy powder) is preferably used.

  In this way, since the filler powder 2 further includes an Al-Mg alloy powder in addition to the alumina powder or the alumina particles, the surface of the substrate is physically activated by the collision between the filler powder 2 and the substrate 3. In addition, the substrate surface is chemically activated by the reducing action of magnesium (Mg) in the Al-Mg alloy powder, and a nitride layer is efficiently formed on the substrate surface. It becomes like this.

When comparing the oxidation standard free energy G _O of magnesium (Mg) and aluminum (Al), G _{O, Mg} <G _{O, Al} and comparing the nitridation standard free energy G _N , G _{N, Mg} > G _Since it is _{N and Al} , the nitriding reaction of aluminum is promoted by magnesium (Mg) in the Al-Mg alloy powder even if oxygen is present in the reaction system.

Here, the blending ratio (mixing ratio) of the Al-Mg alloy powder with respect to the filling powder 2 (hereinafter simply referred to as Al-Mg / Al ₂ O ₃ blending ratio) is 0.7 mass% or more and 2.0 mass% or less. Is preferred. If it is less than 0.7% by mass, a nitride layer may be formed only on a part of the substrate surface and may not be formed on the entire surface. If it exceeds 2.0% by mass, the nitriding treatment starts and aluminum (Al) and nitrogen (N A rapid exothermic reaction may occur due to the reaction with (a), and the filler powder 2 containing alumina powder or alumina particles as a main component may be sintered.

  As the barrel container 1, one that rotates or swings is used. In rotation, a part of the object to be agitated is in an upper-slip state in the upper layer and is not agitated, whereas in the oscillation, the object is subject to reversal every time the reversing operation is performed. Since the agitated material is agitated so that the upper layer and the lower layer are interchanged and the agitation efficiency is improved, it is preferable to use a rocking one. In addition, due to this rotation or swing, an extra deposited layer that does not participate in the nitriding reaction that adheres to the surface of the base material (the powder powder 2 adheres to the surface of the base material and forms a film) fills the base material 3. The effect removed by the collision with the powder 2 is also obtained.

  Here, as shown in FIG. 1 (b), the swing angle θ, which is the maximum angle at which the swing operation centering on the point O swings to the left and right, is determined by the amount contained in the barrel container 1 when the swing operation is reversed. From the viewpoint of minimizing the time zone during which no stirring is performed and from the viewpoint of reducing the deposited layer adhering to the surface of the base material, a larger angle up to 300 ° is preferable. In general, the angle is preferably about 270 ° from the viewpoint of securing the handling position and operation of auxiliary equipment such as a thermocouple, a gas pipe, and a cooling water channel attached to the barrel container 1.

  In addition, the rocking speed, which is the speed of the rocking motion, increases the difference in motion between the filling powder 2 and the base material 3 and improves the mechanical (physical) stirring effect. The higher it is to sec, the better.

  Furthermore, the swinging operation is preferably pulsating swinging. That is, as shown in FIG. 1 (b), in the middle of the swinging operation, the swinging operation is temporarily stopped at each angular position A to D positioned at a certain angular interval, and the swinging operation is continued. It is preferable that In addition, by making the pulsation fluctuation stopped at a certain angle as short as possible, for example, 1.2 seconds or less in this way, the pulsation fluctuation is constantly subjected to stress and vibration depending on the conditions. And the effect of incorporating nitrogen gas as the processing gas into the filling powder 2 is obtained, and the stirring efficiency and the nitriding efficiency are improved. Here, the fixed angle, that is, the rotation (phase) angle (φ1 to φ3; φ1 = φ2 = φ3, swing angle θ = φ1 + φ2 + φ3) for one pulsation is as shown in FIG. When the swing angle θ is 270 °, 135 °, 90 °, 67.5 °, 45 °, 27 ° or 19 divided by the natural angle 2, 3, 4, 6, 10 or 14 ° can be. In the barrel container 1 shown in FIG. 1B, the rotation angle (φ1 to Φ3) for one pulsation is 90 °.

  Further, the barrel container 1 is preferably in the shape of a polygonal column, and preferably in the shape of an octagonal column as shown in FIG. Thus, when the barrel container 1 has a polygonal columnar shape, preferably an octagonal columnar shape, even if the rocking speed is increased, a sliding phenomenon that becomes noticeable at that time, that is, the filled powder 2 is applied to the wall of the barrel container 1. The resulting slip phenomenon can be effectively suppressed by temporarily holding the filling powder 2 on the polygonal surface, and the stirring efficiency can be maintained high.

  In the nitriding method according to the present invention, the nitriding treatment temperature (temperature in the barrel vessel 1) is preferably 610 ° C. or more and 640 ° C. or less from the viewpoint of forming a nitride layer on the entire surface of the substrate. . When the temperature is lower than 610 ° C., the nitriding treatment, that is, the change from the deposited layer to the nitride layer may be insufficient, and when the temperature exceeds 640 ° C., the substrate 3 may be melted.

  In the nitriding method according to the present invention, the nitriding treatment time is preferably 3.4 hr or more and 7 hr or less from the viewpoint of sufficiently growing the nitride layer on the surface of the substrate and ensuring the thickness. If the time is less than 3.4 hours, a nitride layer may not be formed on the surface of the substrate. If the time exceeds 7 hours, the aluminum nitride content (generation rate) in the nitride layer decreases, and the hardness and wear resistance are insufficient. There are things to do.

Hereinafter, the present invention will be described more specifically with reference to examples.
<Example 1>
In Example 1, the influence of the treatment temperature and the Al—Mg / Al ₂ O ₃ blending ratio with respect to the filling powder 2 on the formation of the nitride layer on the substrate surface was examined.

Here, industrial pure aluminum (symbol A1050) was processed into a rectangular parallelepiped shape (block shape) of 40 mm × 20 mm × 5 mm by wire electric discharge machining to obtain a substrate 3. In addition, alumina (Al ₂ O ₃ ) powder with an average particle size of 100 (mm) (made by Showa Denko KK, white alumina abrasive, White Morundum WA) and an Al-Mg alloy with an average particle size of 200 (mm) Powder (Rare Metallic Co., Ltd., Al-50 mass% Mg) was mixed at a blending ratio of 0.7, 0.8, 0.9, and 1.0 mass% to obtain Filled Powder 2.

As shown in FIG. 2, the surface nitriding apparatus for aluminum material of the first embodiment is an octagonal barrel container 1 supported on a gantry 4 so as to be able to rotate (swing), and the barrel container 1 is attached to a belt 5 and a pulley. 5a, 5a, a servo motor 7 as a barrel container oscillating means electrically connected to the pulse generator 6 to oscillate through 5a, 5a, and nitrogen (in the barrel container 1 through a gas path pipe 8a). N ₂ ) Controlled by a temperature controller 9 having a mass flow controller 8 as a processing gas introduction means for introducing gas, and a thermocouple 9 a for measuring the temperature of the filled powder 2 in order to heat the inside of the barrel container 1. And a heater 10 which is connected in a possible manner.

  Here, the barrel container 1 was an octagonal cylinder having an inner diameter of 151 mm and an overall length of 240 mm. Moreover, the mass of each base material 3 was 10 g (size: 40 mm × 20 mm × 5 mm), and the total mass of the filling powder 2 was 1000 g (the filling rate in the container was 14.9%).

Then, as shown in FIG. 2, the five base materials 3,... And the filling powder 2 were accommodated in the barrel container 1 in which the set temperature of the heater 10 was set to 610 ° C. or 630 ° C. by the temperature controller 9. After that, nitrogen (N ₂ ) gas is introduced into the barrel container 1 at a rate of 100 cm ³ / min with the mass flow controller 8 to replace the air in the barrel container 1 and wait for the temperature of the barrel container 1 to rise. It was left as it was for 30 minutes. Further, when the temperature controller 9 confirmed that the temperature increased to each processing temperature, nitrogen gas was again introduced into the barrel container 1 at 900 cm ³ / min. Furthermore, the pulse generator 6 and the servo motor 7 set the swing angle θ to 270 °, the swing speed to 72 ° / sec, and the pulsation rotation (phase) angle (φ1 to φ3) to 90 °. The nitriding treatment (surface nitriding step) of the present invention was performed for 5 hours. Thereafter, the introduction of nitrogen gas and heating by the heater 10 were stopped, and the barrel container 1 was allowed to cool naturally.

As a result, the relationship shown in FIG. 3 was obtained for the processing temperatures of 610 ° C. and 630 ° C. Here, the straight line in FIG. 3 was obtained by linear approximation (least square method). Further, when the Al—Mg / Al ₂ O ₃ blending ratio was 0.7% by mass, the formation of a nitride layer was confirmed only on a part of the substrate surface by EPMA (Electron Probe Micro Analyzer). Then, the nitride layer thickness at the 0.7 mass% was set to 0 μm. Further, when the Al—Mg / Al ₂ O ₃ blending ratio exceeded 2.0 mass%, the filled powder 2 was sintered.

As shown in FIG. 3, in the range where the melting of the base material 3 and the sintering of the filling powder 2 do not occur (below 653 ° C., see FIG. 6), the nitride layer increases as the Al—Mg / Al ₂ O ₃ blending ratio increases. It was confirmed that the thickness (μm) increased and the growth rate of the nitride layer increased. This confirmed the activation effect of the substrate surface by the Al-Mg alloy powder. Further, FIG. 4 shows an optical micrograph of the cross section of the surface layer of the base material obtained when the processing temperature is 630 ° C.

The optical micrograph shown in FIG. 4 was obtained by processing the base material 3 by the method shown below in order to observe the state of the cross section of the surface layer of the base material 3 and photographing the resulting cross-sectional portion with an optical microscope. It is. That is, the base material 3 is ultrasonically degreased and washed with acetone and then embedded in an epoxy resin using a micro press. Next, the processed portion is cut with a fine cutter, and the obtained cross-sectional portion is wet-polished with # 220 to # 2000 emery paper. Then, the cross section is buffed with an α-Al ₂ O ₃ abrasive (particle size 0.5 μm) to finish a mirror surface.

Moreover, when the Vickers hardness Hv of the nitride layer was examined for the Al-Mg / Al ₂ O ₃ blending ratios of 0.8% by mass and 1.0% by mass, the results of 200Hv to 300Hv were obtained with the 0.8% by mass. On the other hand, in the case of 1.0% by mass, results of 300 Hv to 600 Hv were obtained. From this, when the Al-Mg / Al ₂ O ₃ compounding ratio is in the range of 0.7% by mass or more and 2.0% by mass or less, the higher the Al-Mg / Al ₂ O ₃ compounding ratio, the higher the hardness of the nitride layer. Was confirmed.
<Example 2>
In Example 2, the influence of the amount of filled powder on the formation of a nitride layer on the substrate surface was examined.

Here, the mixing ratio of Al-Mg / Al ₂ O ₃ is 1.0 mass%, and the amount of filled powder is 1000 g (14.9% filling rate in container), 2000 g (29.8% filling rate in container), 3000 g (filling rate in container 44.7%) The nitriding treatment of the present invention was performed in the same manner as in Example 1 except that the nitriding treatment was performed. As a result, the relationship shown in FIG. 5 was obtained for the nitride layer thickness and the amount of each filled powder.

From FIG. 5, it was confirmed that the growth rate of the nitride layer changes with the change in the amount of the filling powder. It can be presumed that this is because the movement state of the base material 3 (the stirring state of the base material 3 in the barrel container 1) changes and the growth rate of the nitride layer changes when the amount of filled powder changes. In addition, by the rocking | fluctuation of the barrel container 1, the upper layer part of the filling powder 2 forms the collapsing layer 2a (fluidized bed) (refer Fig.1 (a)). In general, when the amount of the filling powder in the barrel container 1 is small, the ascending force of the filling powder 2 when the collapsing layer 2a collapses is small and the mechanical frictional force is small. . On the other hand, when the amount of the filled powder is increased, the collapsing layer 2a becomes thin, but the residence time of the base materials 3, ... other than the collapsing layer 2a becomes long, and the corners of the base material 3 are ground. From this, it is generally considered that the volume ratio (filling rate) of the base material 3 and the filling powder 2 to the barrel container 1 is preferably 50% to 60%. It was confirmed that the growth rate of the nitride layer was the highest when the filling rate was 14.9%.
<Example 3>
In Example 3, the influence of the treatment temperature on the formation of the nitride layer on the substrate surface was examined.

Here, the same as in Example 1 except that the Al—Mg / Al ₂ O ₃ blending ratio is 1.0 mass% and the set temperature of the heater 10 is changed to 590, 600, 610, 620, 630, 640 ° C. The nitriding treatment of the present invention was performed. As a result, the relationship shown in FIG. 6 was obtained for the nitride layer thickness and the processing start temperature (processing temperature).

As shown in FIG. 6, in the range where the melting of the base material 3 and the sintering of the filling powder 2 do not occur (less than 653 ° C.), the growth rate of the nitride layer was improved as the treatment temperature was higher. Here, the straight line in FIG. 6 was obtained by linear approximation (least square method). Referring to FIG. 6, when the processing start temperature is 653 ° C., a rapid heat generation occurs due to the reaction between aluminum (Al) and nitrogen (N) immediately after the processing starts, and the temperature inside the container exceeds the melting point of aluminum (659 ° C.). Rose and the substrate 3 melted. A nitride layer was formed on a part of the substrate surface at a treatment temperature of 607 ° C., but no nitride layer was produced on the entire substrate surface. Therefore, in FIG. 6, the nitride at the treatment temperature of 607 ° C. was used. The layer thickness is 0 μm.
<Example 4>
In Example 4, the influence of the treatment time on the formation of the nitride layer on the substrate surface was examined.

Here, the Al—Mg / Al ₂ O ₃ blending ratio was 1.0 mass%, the treatment temperature was 630 ° C., and the barrel nitriding treatment time was changed to 1, 3, 4, 5, 6, 7 hr. The nitriding treatment of the present invention was performed in the same manner as in Example 1. As a result, according to the observation with an optical micrograph, the formation of the nitride layer could not be confirmed at the processing time of 1 hr and 3 hr, but the nitride layer was formed on a part of the substrate surface at 3.4 hr, and at 4 hr. It was confirmed that a nitride layer was formed on the entire surface of the substrate, and that it grew as the treatment time was extended.

  As a result, the Vickers hardness Hv of the nitride layer obtained at the treatment times of 4, 5, 6, and 7 hours was 533, 422, 385, and 299 Hv, respectively, and a tendency to decrease as the treatment time increased was confirmed. This agreed with the result of the weight ratio of nitrogen and aluminum in the nitride layer separately measured by XRD (X-ray diffraction). That is, it was also confirmed that the Vickers hardness Hv of the nitride layer decreases as the content of aluminum nitride decreases in the nitride layer.

Here, the intensity ratio of AlN (aluminum nitride) and Al (aluminum) was determined from the intensity of the diffraction peak obtained by XRD on the surface of the nitride layer. Here, the strength of the plane index (hkl) in the nitride layer (constituent phase X) is defined as I _{X (hkl),} and the strength ratio of AlN and Al is defined as _{IR , AlN} and _{IR , Al ,} respectively. , I _{R, AlN} and I _{R, Al} are represented by the following formula 1.

The above results are summarized in Table 1 below.

From Table 1 above, when the treatment time exceeds 7 hours, the content (generation rate) of aluminum nitride in the nitride layer decreases. Along with this, Vickers hardness Hv decreased from 299, confirming that hardness and wear resistance were insufficient.

Further, according to EPMA element mapping analysis and line analysis for each sample, it was confirmed that nitrogen was uniformly distributed in the nitride layer and no oxygen was contained.
According to the observation by EPMA, at the treatment time of 3 hours, only the base material surface became white, and the concentration of magnesium (Mg) was observed on the base material surface. Thereby, it can be estimated that magnesium is solid-dissolved on the surface of the base material, and this solid solution layer is involved in the formation of the nitride layer in the nitriding treatment for 4 hours or longer.

FIG. 7 shows the relationship between the obtained nitride layer thickness and the square root of the nitriding treatment time. As shown in FIG. 7, it can be seen that the nitride layer thickness increases in proportion to the square root of the processing time after the incubation period t ₀ . Further, from this, it was confirmed that the growth of the nitride layer was due to the diffusion control of aluminum or nitrogen into the deposited layer or nitride layer.

Furthermore, from FIG. 7, according to the nitriding treatment of the present invention, the growth rate of the nitride layer is about 180 μm / hr, which is compared with the growth rate of the nitride layer obtained by ion nitriding treatment, from 0.5 μm / hr to 2 μm / hr. Then, it was confirmed that the nitride layer could be formed on the substrate surface at a higher speed. Furthermore, it can be confirmed from FIG. 7 that the latent period t ₀ during which no nitride layer is generated is t ₀ = 3.4 hr.

The present invention can be appropriately changed in design without departing from the technical idea thereof, and is not limited to the above-described embodiments and examples.
For example, in the above embodiments and examples, alumina powder (Al ₂ O ₃ powder) as the packing powder 2 and an aluminum - magnesium alloy powder (Al-Mg alloy powder) and the mixture of _{(Al-Mg / Al 2 O} 3 filler powder ), But pure alumina powder can also be used.

(A) is principal part sectional drawing which shows the stirring state of the base material and filling powder in a barrel container, (b) is explanatory drawing which shows the rocking | swiveling angle etc. of a barrel container. The apparatus block diagram which shows the surface nitriding apparatus of an aluminum material. Graph showing the relationship between the nitride layer thickness ([mu] m) and Al-Mg / Al ₂ O ₃ composition ratio (% by weight). The optical microscope photograph which shows the surface layer cross section of the base material after a nitriding process. The graph which shows the relationship between nitride layer thickness (micrometer) and filling powder amount (g). The graph which shows the relationship between nitride layer thickness (micrometer) and process temperature (degreeC). The graph which shows the relationship between the nitride layer thickness (micrometer) and the square root (hr1 ^{/ 2} ) of the processing time of nitriding.

Explanation of symbols

1 ... barrel container, 2 ... filling powder _{(Al-Mg / Al 2 O} 3 filler powder), 3 ... substrate (aluminum material).

Claims (6)

A method for producing an aluminum member having improved wear resistance by forming a nitride layer on the surface of an aluminum material,
In the presence of a processing gas containing nitrogen gas, alumina powder or filled powder containing alumina particles and a base material made of aluminum or an aluminum alloy are mixed in a rotating or swinging barrel container, and the surface of the base material is mixed. A method for producing an aluminum member, comprising a surface nitriding step of forming a nitride layer.   2. The method for manufacturing an aluminum member according to claim 1, wherein the barrel container swings and is formed in a polygonal column shape.   The manufacturing method of the aluminum member of Claim 1 or Claim 2 WHEREIN: Al-Mg alloy powder is contained with the compounding ratio of 0.7 mass% or more and 2.0 mass% or less with respect to the said filling powder.   The aluminum member manufacturing method according to any one of claims 1 to 3, wherein in the surface nitriding step, a treatment temperature is set to 610 ° C or higher and 640 ° C or lower to form a nitride layer on the surface of the substrate. Manufacturing method of member.   The aluminum member manufacturing method according to any one of claims 1 to 4, wherein in the surface nitriding step, a treatment time is set to 3.4 hours to 7 hours and a nitride layer is formed on the surface of the base material. Manufacturing method. A surface nitriding device for an aluminum material for forming a nitride layer on the surface of the aluminum material and improving the wear resistance of the surface of the aluminum material,
A barrel container in which a filling powder containing alumina powder or alumina particles and a base material made of aluminum or an aluminum alloy are accommodated, a processing gas introduction means for introducing a processing gas containing nitrogen gas into the barrel container, and the barrel container A surface nitriding apparatus for an aluminum material, comprising barrel container swinging means for swinging the barrel container at a predetermined angle while introducing a processing gas therein.