JPS6050138A - Heat- and wear-resistant high-strength aluminum alloy member of hard particle dispersion type and its production - Google Patents

Abstract

PURPOSE:To obtain an Al alloy member having excellent resistance to heat and wear by dispersing and solidifying a molten Al alloy contg. a specific ratio of Si and Ni by quick cooling to form powder, mixing hard particles therewith under specific conditions and subjecting the mixture to hot extrusion. CONSTITUTION:A molten alloy contg., by weight, 10.0-30.0% Si, 5.0-15.0% Ni, and if necessary contg. 0.5-5.0% Cu and 0.1-2.0% Mg and consisting of the blance inevitable impurities and Al is dispersed and solidified by quick cooling to form powder. Hard particles (metallic Si particles, etc.) having the higher hardness than the powder and having <=60mu average grain size are mixed at 2-20wt% with said powder and the mixture is subjected to hot extrusion at >=extrusion ratio. The Al alloy member of the structure in which the hard particles having the higher hardness than the Al matrix, having the average grain size larger than the grain sizes of the Si crystal and intermetallic compd. and having <=60mu are dispersed in the Al matrix having <=15mu Si crystal grain size and haing <=20mu grain size of the intermetallic compd. dispersed finely therein is thus obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a heat-resistant and wear-resistant high-strength aluminum 11 alloy member suitable for members such as cylinder liners of internal combustion engines and vanes of rotary compressors for car coolers, and a method for manufacturing the same.

Replacing the cylinder block of an automobile engine from cast iron to an aluminum alloy casting has the effect of reducing weight, but even in this case, the inner circumferential side that slides with the screw 1 link and piston is not wear resistant if the aluminum 11 alloy casting is used. Because of the insufficient amount of carbon, cylinder liners made of flaky graphite cast iron are covered with rust and used as bushes. By using aluminum alloy for this cylinder liner, you can achieve further weight reduction, and
Its thermal conductivity is better than cast iron, and its coefficient of thermal expansion is larger than that of cast iron, and is close to that of the aluminum alloy casting of the cylinder block, so the adhesion between the liner and plotter is maintained even at elevated temperatures during operation. This makes it possible for the engine to have good heat dissipation, which lowers the inner wall temperature of the liner, thereby extending the life of the lubricating oil, and allowing the use of low-viscosity lubricating oil, which improves fuel efficiency. It is expected to be effective.

In addition, since high-Si aluminum alloy has a larger coefficient of thermal expansion than cast iron, it is possible to set the clearance between the aluminum alloy and the piston smaller, and reducing the clearance between the piston and the piston will improve fuel efficiency. ―
In addition, the consumption of lubricating oil can be reduced. In addition, since high-Si aluminum alloy has a low coefficient of friction,
It is expected that fuel efficiency will improve as friction loss between the engine and the Henlink is reduced.

Although there are many advantages to using aluminum 11 alloy for cylinder liners, conventionally known aluminum alloys are insufficient as cylinder liner materials for cast-in applications. For example, A390 with ΔC standard. O alloy (Si:
16-18%, Cu: 4 to 5% r M g
: O-50□ 0-65%, F”e:0
．． 5%, Ti: 0.2%, 7. n: O, 1%, remainder: Al) has a wide solid-liquid coexistence temperature range, so
In order to obtain sound castings, a large feeder is required, resulting in poor yields and high loss 1. In addition, primary Si grains are still coarse even with refinement treatment and mold casting methods. Poor machinability. Another fatal drawback is that the material is softened by heat when it is cast into the cylinder block, resulting in significantly lower wear resistance, and the workpiece surface is prone to chattering and cracking, making honing difficult. Furthermore, in recent years, a technique has been proposed in which powder metallurgy is used to make a hollow body by hot extruding an alloy having a composition close to A390.0 into powder (Japanese Patent Laid-Open No. 52-109'115). This is a method to obtain a hollow body by hot extruding fine particles or powder that are rapidly cooled by a high-Si aluminum alloy melting method or atomization method using centrifugal force. This manufacturing method has a much better weight yield than the hollow bodies obtained by the method.In addition, this method has primary Si grains with a size of 20 μm or less, so it has excellent ductility and machinability. It also has the characteristic of a low coefficient of friction unique to the 1' elemental Δ1 alloy.In addition, by this method, 15 to 20% Si and 1 to 5% Cu can be obtained.

An alloy of 0.5 to 5% Mg, 0.5 to 1.5% Ni, and the balance A1, or S i C, Sn, Alt'!
! A hollow body made by mixing and extruding has been proposed.

When we conducted this 1-race experiment, we found that 20
．． 08i-4,0Cu-0,8Mg-0,5N i −
A cylinder liner (
Outer diameter: 73 mm Inner diameter: 65 nt m Height: 105 m
As a result of a test using the diamond casting method at a molten metal temperature of 675°C on an ADC-12 alloy cylinder block (weight 3./IKg), it was found that T6
It was found that the hardness of +-I R880 due to treatment softened to about HRB40 after casting. Therefore, this hollow body also becomes soft when it is wrapped in an aluminum alloy cylinder block, making it unusable as a cast-in cylinder liner.

In addition, casting is performed using the diamond casting method or low-pressure casting method, and it is desirable to make the liner as thin as possible from a cost perspective. The liner becomes easily deformed due to mechanical stress applied during the liner transportation process and positioning.

The present inventors have solved these drawbacks of conventional aluminum alloys, and have found that they do not soften even under the heat load applied during casting, and furthermore, their hardness does not decrease even under the heat load during use. We have developed and previously proposed a heat-resistant, wear-resistant, high-strength aluminum alloy and its manufacturing method that minimizes the occurrence of
Japanese Patent Application No. 1987=1], No. 9901, Japanese Patent Application No. 1987-11
No. 9902).

Regarding the high potassium aluminum 11 alloy proposed in the future,
In order to improve its high-temperature strength, fine particles of intermetallic compounds containing elements such as Fe, Mn, and Ni, which have a slow diffusion rate in Al, are finely dispersed in the alloy matrix. As a result of engine tests, it was found that cylinder liner wear tends to increase when dust or carbon particles, which are combustion products, are mixed into the lubricating oil. In addition, when testing this type of alloy phase as a vane for a rotary compressor for a car cooler, it was found that wear increases when the surface roughness of the sliding member is rough.

This invention was made with the aim of further improving the wear and seizure resistance properties of the aluminum 11 alloy and solving the above-mentioned difficulties. 15.0% and further Cu as necessary.
0.5 to 5.0% and Mg-0.2 to 3.0%, the remainder is A1 containing unavoidable impurities, the size of Si crystal particles is 15 μm or less, and the size of intermetallic compound particles is Hard particles having a hardness higher than that of the base, having a particle size larger than that of the Si crystal particles and intermetallic compound particles, and having a particle size of 60 μrn or less, which are dispersed in a finely divided aluminum alloy base having a size of 20 μm or less. The present invention relates to a hard particle-dispersed heat-resistant, wear-resistant, high-strength aluminum alloy having a structure in which 2 to 20% (heavy weight) of is dispersed, and further provides a method for producing the aluminum alloy.

The present invention will be further explained below.

First, the reason for limiting the components of the alloy of the present invention excluding the hard particles will be explained.

When Si is less than 10%, there are few dispersion plates of Si crystal particles,
The effect on wear resistance is insufficient.

In the hypoeutectic region around 5ilO%, primary Si cannot be crystallized and has a fine eutectic structure. As the amount of Si added increases, St begins to crystallize as an initial product, resulting in an improvement in heat resistance and wear resistance.

However, if the Si content exceeds 30%, it becomes extremely difficult to mix it with hard particles, which is the gist of the present invention to be described later, and hot extrude it. In addition, when using an aluminum alloy cylinder block as a cylinder liner, etc., the coefficient of thermal expansion decreases with the addition of Si, and S
If i exceeds 30%, the adhesion with the cylinder block material may deteriorate or it becomes necessary to increase the clearance with the piston. Therefore, for the addition of Si, 10.0~
The content is preferably 30.0%, preferably 12.0 to 23.0%.

Ni is an important component in the alloy of the present invention, and Al
Utilizing its low solubility and slow diffusion rate, it is dispersed in the matrix as a fine intermetallic compound, and is particularly added as a one-to-one addition to enhance high-temperature strength. If Ni is added in excess of the solid solubility limit, it will precipitate as an Al-Ni intermetallic compound, and its shape will become coarser as the amount added is larger and the cooling rate is slower. These intermetallic compounds exist as rod-shaped structures in the alloy powder obtained by the dispersion and rapid solidification method, which is an important aspect of the present invention, and are divided by the subsequent hot extrusion process. distributed to This type of intermetallic compound is stable and difficult to grow even at high temperatures, and therefore exhibits the effect of maintaining the hardness of the t-alloy at a high value by maintaining the temperature at a high temperature for a long time. Therefore, unlike cast-in cylinder liners, there is no decrease in hardness even after exposure to high temperatures, and it maintains good wear resistance.
It becomes f-ability.

No significant effect was observed when the amount of Ni added was less than 5%.
If it exceeds 15%, the solubility limit of Si in A1 becomes low, and excess Si becomes the initial product and crystallizes in large quantities. Furthermore, the melting temperature of the alloy becomes high and the oxidation of the molten metal progresses, requiring special measures to prevent oxidation, which is not economical. In addition, the precipitated intermetallic compound becomes coarse, and when it is divided and refined by hot extrusion processing to form an armor, the extrusion processability also deteriorates.

(-tL, therefore, the amount of Ni added is preferably in the range of 5.0-15.0%.

In the alloy of the present invention, Ni in the amount of ε is added to form a forced solid solution in the aluminum alloy powder, and after being weighed out as a rod-shaped intermetallic compound, fine particles are formed by hot extrusion in the post-processing step. By precipitating it as a compound or dividing it, it is finely dispersed in the aluminum alloy matrix and improves the strength of the material, especially the strength and hardness at high temperatures.

In addition, in the present invention, 0.5 to 5.0 as necessary.
% Cu and 0.2-3.0% Mg can be added. Cu and Mg are known as components that impart age hardenability to aluminum alloys and strengthen the material. Also in the present invention, adding Cu and Mg within the above-mentioned range of 1 degree within the solid solubility limit P at the solution treatment temperature is effective for strengthening the material. Furthermore, in the present invention, Fe.

In addition to adding Mn, Ti, Cr, V, Zr+ Mo, Co, etc., a particularly important requirement in the present invention is that the aluminum alloy matrix contains primary Si grains which have a hardness higher than that of the matrix and whose grain size is described later. 2 to 20% hard particles larger than the particle size of the intermetallic compound particles and smaller than 60 μm, total 20%
Is Rukoto.

This 11. Since the hard particles are dispersed in the aluminum alloy base, they are exposed to the sliding part during sliding and facilitate the formation of an oil film even under low-speed sliding conditions. It exhibits good wear resistance even when the lubricating oil is rough or contains dust or carbon particles.

Oxide, 7N compound such as TiC, 1°i Si2, M
Intermetallic compounds such as o S i , ceramics such as borides, and powders of hard alloys such as ferromolybdenum and ferrotanksten can be used. Among these four hard powders, the metals Si, Si3N4 and SIC in particular have a specific gravity close to that of the alloy powder obtained by the above-mentioned dispersion and rapid solidification method, so they are unlikely to cause segregation in the manufacturing process of the alloy of the present invention. Al-Si
It is advantageous because it has good adhesion to alloys and is inexpensive.

In order to improve the wear resistance under the low-speed sliding strip 1, the particle size of the hard particles is determined by adjusting the particle size of the primary Si crystal grains and intermetallic compound particles that are finely dispersed in the Aluminum 15 Imakane matrix. It needs to be larger than the diameter. However, if it is larger than 60 μm, hot extrusion processing becomes difficult, so it should be at most 60 μIr1 or less, preferably 40 μm or less.

When these hard particles are mixed with aluminum alloy powder obtained by the dispersion rapid solidification method and hot extruded, they are subjected to a large compressive force from the surroundings by the alloy powder, so they adhere well to the alloy and do not slide easily. There is no possibility that the molded object will peel off or fall off inside.

It should be noted that these hard particles can be used alone or in combination depending on the hardness, surface roughness, sliding conditions, etc. of the mating sliding material.

If the total amount of these hard particles is less than 2%, the above effect is insufficient, and if it exceeds 20%, extrusion processing becomes difficult and cracks are likely to occur in the extruded product.Therefore, In the present invention, the amount of the hard particles is in the range of 2 to 20%.

The reason why the size of the Si crystal grains is set to 15 μrn or less is not only for the manufacturing requirement of facilitating extrusion processing, but also for improving the ductility of the resulting alloy and improving the machinability.

In addition, the fine crystals of Si improve wear resistance and reduce the coefficient of friction, making it suitable for sliding parts +4 such as cylinder liners.

The size of the Al-Ni intermetallic compound powder is essentially 5 μm or less, and even large particles can be finely and uniformly dispersed to a diameter of 20 μm or smaller, resulting in higher high-temperature strength and wear resistance than conventional products. Significant improvement in comparison.

The hard particle-dispersed heat-resistant, wear-resistant, high-strength aluminum alloy member of the present invention is dispersion-strengthened by the Wi-refining dispersion of the intermetallic compound mentioned above, and has particularly improved high-temperature strength.
By dispersing hard particles having a grain size larger than those of these intermetallic compound phases and Si crystal grains into an aluminum alloy base whose wear resistance is improved by the fine dispersion of crystal grains, parts can be improved. The wear resistance and seizure resistance of this product have been further improved, and in addition to being superior in wear resistance compared to conventional products, the material does not soften even if subjected to heat history due to casting etc. This makes it particularly suitable for use as cylinder liners for internal combustion engines, parts of rotary compressors for car coolers, etc., which are subject to severe operating conditions.

The present invention further provides a method for manufacturing the above-mentioned hard particle dispersed heat-resistant, wear-resistant, high-strength aluminum alloy member.

The gist of the manufacturing method is that a high-Si aluminum alloy molten metal containing a predetermined amount of Ni is dispersed and rapidly solidified, a predetermined amount of hard particles are added to the obtained aluminum alloy powder, mixed, and then hot extrusion molded. It's about doing.

Si disperses and rapidly solidifies the melted alloy.

This is to form a supersaturated solid solution of alloying elements such as N i y Cur M g and to refine primary Si and intermetallic compound phases. The method of dispersion and rapid solidification is as follows:
Known metal powder manufacturing methods such as atomization and centrifugal pulverization can be used. These methods reduce the powder particle size to 0.5m.
An alloy powder with a satisfactory structure can be obtained by refining the powder to a size smaller than m and rapidly solidifying it. Next, 2 to 20% of the hard particles described above are added to the aluminum alloy powder and mixed. Although it is permissible for some small-sized particles to be mixed into the hard particles, in order to improve wear resistance and seizure resistance, dispersed crystals are generally added to the alloy powder obtained by the above-mentioned dispersion and rapid solidification method. It is desirable that the Si crystal grains and intermetallic compounds that have come out or dispersed and precipitated are larger than the particle size that will occur after extrusion processing.
Further, from the viewpoint of moldability, it is desirable that the thickness be 60 μm or less.

In addition, it is desirable to add a step of manufacturing a billet before hot extrusion, and when manufacturing this by compression molding in a mold, the mold and powder material are
Do this at a temperature of around ℃. If the temperature exceeds 300°C, oxidation becomes significant, so it is preferable to carry out the process in a non-oxidizing atmosphere such as nitrogen gas or argon. Molding pressure is 0.5
From the viewpoint of handling of the green compact, it is preferable to carry out the drying at a pressure of about 3 to 3 cm/cnf, and to set the green compact density to 70% or more of the true density ratio.

It is also possible to form the billet 1 by cold isostatic pressing, but in this case a pressure of 5 siro/am2 or higher is required.

Hot extrusion is carried out at a temperature of 350°C or higher, preferably 400°C or higher.
Perform at a temperature range of 470°C. This is to facilitate the molding process of the green compact and at the same time promote bonding between particles to form a strong compact.

Furthermore, the intermetallic compound forming a rod-like structure is divided into fine particles and dispersed, thereby improving the strength and friction characteristics of the molded article. Hot extrusion is preferably carried out by preheating the green compact (billet) in the air or in non-oxidizing fJ 1111 air, and then inserting it into a container at the same temperature.

Further, the extrusion processing ratio is preferably 10 or more. If the extrusion processing ratio is less than 10, voids remain in the extruded material, and materials with high strength and toughness cannot be obtained because the diffusion bonding between powders and the separation effect of rod-shaped intermetallic compounds are insufficient. It is.

According to the method of the present invention, the aluminum alloy powder obtained by the dispersion rapid solidification method contains the above-mentioned alloying elements in supersaturated solid solution4, as well as extremely fine primary Si crystal grains and rod-shaped intermetallic compounds are precipitated, and the above-mentioned metal Si particles, 813 N4 particles or S
i By mixing a predetermined amount of hard particles such as CR particles and performing hot extrusion, the rod-shaped intermetallic compound is divided into extremely fine pieces and dispersed finely and uniformly, while the mixed hard particles are With almost no change in diameter, the particle size is larger than that of the primary Si crystals and the fragmented intermetallic compound particles, and is distributed throughout the base, contributing to further improvement of the wear resistance and seizure resistance of the monthly charge. do.

Example 1 Molten high-Si aluminum alloys having various alloy compositions shown in Table 1 were air atomized to rapidly solidify powders, and the resulting powders were sieved to -60 mash and J7. Next, hard powder as shown in A-1 was blended with the rapidly solidified alloy 1'51 powder, and mixed uniformly in a V-shaped cone mixer with nitrogen gas. The metal Si used as hard particles had a purity of 98.5% and a particle size of 15μIn, and SrN had an average particle size of 20μm.
C is a QC type with an average grain size of 10 μm.

These mixed powders were heated to 250°C for 1 hour, filled into a three-part mold with an inner diameter of 87 mm heated to the same temperature, and compression-molded using a 1-do punch to form a mold with a length of 200 r with a true density of 72%.
It was made into a billet from N River.

Next, the fillets 1~ were heated in Ar gas at 450°C for 30 minutes, then inserted into a container with an inner diameter of 90mm heated and maintained at 430°C, and made into round bars by indirect extrusion using a die with an inner diameter of 23mm. It was made into an extruded material. The extrusion ratio is 15.3. ? ! ) Extruded material 350°C Alloy (cast material) A39
A tensile test was conducted on a 0-treated material of AC311 alloy, which is a spun aluminum alloy for pistons that has superior heat resistance to 0°0 alloy. The results are shown in Table-2. As is clear from Table 2, the alloy of the present invention has high high temperature strength and high hardness after being held at high temperature.

Next, wear tests were conducted on these alloys.

The test was conducted using the method shown in Figure 1. Exam No. 1 (X)
is held in the test piece holder (2), and the other rotating disk (3)
The lubricant is pressed against the outer peripheral surface of the lubricant at a constant pressure, and the lubricant is supplied from the lubricant supply pipe (4).

The test piece had a prismatic shape of 5 x 5 x 20 mm, and the tip sliding surface was rounded with a radius of (-1).
M polished finish has been applied. The mating disk (3) is made of spheroidal graphite cast iron FCD50 which is hardened and tempered to have a hardness of II RC50, and has an outer diameter of 44.2 mm, and a sliding outer peripheral surface with a surface roughness of approximately 1.5 μII; It has a polished finish. With this kind of device, the mating disc (3) can be moved 1°3.5m/
The test piece (1) was placed on the mating disk (3) while rotating at a circumferential speed of 1.2 seconds and supplying compressor oil (Suniso 5GS) heated to 80 ± 1°C from the supply pipe at a rate of 300 ml/7 minutes. Press it against the outer circumferential surface with a pressing force of 3 kg/mm,
The friction distance was 150 km, and the test piece (1) and the mating disk (
3) and was slid.

As test materials, test pieces (1) were cut out from the extruded round bars of Examples 1 to 3 of the present invention and then subjected to zero treatment, and for comparison, test pieces (1) were cut out from the extruded round bars of Examples 1 to 3 of the present invention, and for comparison, A test piece was cut from the extruded round bar to which no hard powder had been added in 3 and subjected to the same heat treatment and tested. The results are shown in FIG. Note that the amount of wear is indicated by the amount of wear at the tip of the test piece.

As is clear from Fig. 2, the extruded materials of Comparative Examples 1 to 3 without the addition of hard lfl powder particles have more wear groups than the alloys of the present invention with hard powder particles added, and the This shows a tendency for wear to increase in this area. On the other hand, alloys 1 to 3 of the present invention to which hard powder particles were added showed stable and good wear resistance from low speed range to high speed range, and showed a wide range of resistance compared to Comparative Examples 1 to 3. This shows the effect of improving wear resistance.

In particular, when compared to the addition of metal Si particles, when particles with high hardness such as SiN or SiC are added, there is a tendency for wear to be reduced.

Example-2 15.1%S'j-7.0%Ni-2,5%Cu-1,
A molten alloy consisting of 5% Mg and residual Al was sized to 71 mm in the same manner as in Example-1 to obtain a rapidly solidified powder, which was then sieved through a -(j Q mesh to obtain raw aluminum alloy powder. .

The same metal Si grains, 813 N grains, and SiC grains as used in Example-1 were added to the alloy powder at a total angle of 0°3.5.
10%, 15%, and 20%, respectively, and an extruded material having a diameter of 23 mm was prepared in the same manner as in Example-1. The extrusion ratio was 15.3. Test pieces were cut out from these extruded materials and subjected to wear tests in the same manner as in Example 1 to examine the influence of the blending ratio of hard particles.

The test conditions were that the surface roughness of the mating disk was 0.8 to 1.0 μm and the speed per circumference was 1 m/sec, and the other conditions were as in Example 1 above.
The same is true in .

FIG. 3 shows the results when gold [Si grains were mixed], FIG. 4 shows the results when four Si3N grains were mixed, and FIG. 5 shows the results when 810 grains were mixed. In addition, in the figure,
The amount of wear is expressed as a relative wear value, with the wear value in the case of no hard particles 'T- added as 1.

From these figures, it is recognized that when the blending ratio (addition amount) of hard particles exceeds 3%, the wear base is significantly reduced. Note that the extruded material containing 20% Si 3 Nt particles had poor workability and could not be processed into a test piece.

Example 3 Metallic Si grains, Si3N4 grains, and Si0 grains having different average particle diameters were mixed in an amount of 5'X by weight to the same raw material aluminum alloy powder as used in Example 2. Hot extrusion was carried out in the same manner as in Example 1, and wear test pieces were cut out from the obtained extruded material, heat treated in the same manner as in Example 1, and then subjected to the same wear test as in Example 1. Other test conditions were the same as in Example 1.

The results are shown in FIG. As is clear from Figure 6, 1;
, SiC grains and S1qN4 with an average grain size of 1μII+ or less
When particles are added, the wear base becomes large, and even when the particle size exceeds 30 μm, the amount of wear tends to increase, albeit slightly.

This test result is considered to teach the following points. That is, the metal 81 dispersed in the structure of the extruded material
The average particle size of hard particles such as particles, S;, N, particles, etc.
If it is smaller than the value indicating the surface roughness of the mating sliding part 1,
During sliding, these hard particles are likely to be ripped off by the opposing sliding surface. Therefore, qt of the hard particles to be dispersed
It is desirable that the average particle size is not excessively small. - If the particle size of the hard particles dispersed by force is large enough to bridge the adjacent peaks of the unevenness on the surface of the hand sliding portion 411, the hard particles P will peel off and fall off. It is held in a stable state on one side, that is, on the surface of the molded body, and exhibits good wear resistance. However, if the average particle diameter of the hard particles becomes too large, the distance between the hard particles becomes narrow, and wear tends to gradually increase.

As explained above, the hard grain-r/dispersed heat-resistant, wear-resistant, high-strength aluminum alloy of the present invention has high-temperature strength due to dispersion strengthening by fine intermetallic compound particles containing elements with slow diffusion rates in A1. In addition, in the base of the aluminum alloy, whose wear resistance is improved by finely and uniformly dispersed primary crystal Si grains and eutectic Si, there are also fine intermetallic compound particles and primary crystals. It has hard particles having an average particle diameter larger than that of the Si particles dispersed therein, and by having such a structure, it exhibits extremely excellent wear resistance and seizure resistance.

A special feature of the hard grain dispersed heat-resistant, wear-resistant, high-strength aluminum alloy of the present invention is that this alloy has extremely good wear resistance even when aluminum alloy members are used as sliding parts. It means demonstrating.

Mold casting of A'390.0 alloy composition #'J'7 treated material was used as the sliding partner material, one circumferential speed was 5 m/sec, lubricating oil (Suniso 5
GS), the above-mentioned example of the present invention alloy under the condition of oil temperature of 80 ° C.
The wear test of Alloys 1 to 3 (Q-treated material) of Example 1 was carried out in the same manner as in Implementation-1.

For comparison, similar wear tests were also conducted on the alloys of Example 1 of the present invention from which hard particles were removed and the A390.0 alloy (r7 treated material). According to the test results, the hard particle dispersed heat-resistant, wear-resistant, high-strength aluminum alloy of the present invention has significantly superior wear resistance compared to the comparative material and A390.0 alloy, which are made by removing hard particles from the alloy of the present invention. It was confirmed that the product exhibited 1-4 characteristics. Therefore, the aluminum alloy of the present invention can also be used as a sliding member by combining the same types of aluminum alloy members that have conventionally been used as tabs.

[Brief explanation of drawings]

Figure 1 shows the abrasion tester. Figures 2 to 6 show the results of the wear tests. FIG. 7 shows the alloy structure of Invention Alloy 1 in Example 1 (400 times magnification). FIG. 8 shows the structure of the alloy 2 of the present invention in Example 1. Further, FIG. 9 shows the structure of the alloy 3 of the present invention in Example 1. In the diagram: 1. ,,i wear test piece 210. Holder 300. Mating material 510. Metal Si grains 631. Aluminum 11 alloy base 7...S i-s N1 grains 9,..., Si0 grains Applicant Co., Ltd. 1'4 Rikeyu Showa Denko Co., Ltd. Agent Hideaki Kuwabara's X4 Jig X4 ~ East

Claims (3)

[Claims] (1) 5ilO,O~30.0% by weight and Ni5.
O~15.0% and further Cu0.5-5 as necessary
．． 0% and Mg0.2~3.0%, the remainder is made of AI containing unavoidable impurities, the size of Si crystal grains is 15 μm or less, and the size of intermetallic compound powder is 20 μm.
In the aluminum alloy base which is finely dispersed to a size of less than
Larger than the grain size of crystal grains and intermetallic compound powder and 60μ
A hard particle-dispersed heat-resistant, wear-resistant, high-strength aluminum alloy member having a structure in which 2 to 20% (by weight) of hard particles having a particle diameter of rn or less are dispersed therein. (2) The hard particles dispersed in the aluminum alloy base are metal Si particles, S IB N4 particles, and Si
One or two types of C particles f! [Hard particle-dispersed heat-resistant and wear-resistant high-strength aluminum alloy member according to claim 1 comprising one or more (3) Weight ratio Te Si 10.0-30.0% and Ni
5.0-15.0% and 1, further Cu 0 as necessary
．． A molten alloy consisting of Al containing 5 to 5.0% Mg and 0.2 to 3% Mg and the remainder containing unavoidable impurities is dispersed and rapidly solidified to obtain an alloy powder, and the alloy powder is added to the obtained alloy powder. Mixing 2 to 20% (by weight) of hard particles having high hardness and an average particle size of 60 μIn or less,
Hot extrusion molding is carried out at an extrusion ratio of 10 or more.In an aluminum alloy matrix, the Si crystal grain size is 15 μm or less and the intermetallic compound powder is finely dispersed and dispersed in the size of 20 μIn or less. 2 to 2 hard particles having a higher hardness than the base and having an average particle size larger than the particle size of the Si crystal grains and the intermetallic compound powder and 60 μm or less.
A method for manufacturing a heat-resistant, wear-resistant, high-strength aluminum alloy member having a hard particle dispersed structure having a structure in which 20% (by weight) of the hard particles are dispersed.