JPS5913040A - Heat- and wear-resistant high-strength aluminum alloy powder and molded body of said alloy powder and their manufacture - Google Patents

Abstract

PURPOSE:To obtain high-Si Al alloy powder consisting of prescribed percentages of Si and Ni as essential components and the balance Al with inevitable impurities and having superior strength in the temp. range from ordinary temp. to a high temp. CONSTITUTION:Al alloy powder contg., by weight, 10.0-30.0% Si and 5.0- 15.0% Ni or further contg. 0.5-5.0% Cu and 0.2-3.0% Mg is prepared. The powder is rapidly dispersed and solidified by an atomizing method or a means for manufacturing fine powder by centrifugal force to obtain heat- and wear- resistant high-strength Al alloy powder. This Al alloy powder has Si grains of >=15mum size and columnar crystals of an intermetallic compound contg. Ni grown under control, and it is novel alloy powder different from conventional high-Si Al alloy powder. An alloy having said structure can not be obtd. by a casting method.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a high-Si aluminum alloy powder that has excellent strength from room temperature to high temperature, a molded member made of the alloy powder, and a method for manufacturing the same, and particularly relates to a high-Si aluminum alloy powder that has excellent strength from room temperature to high temperature. It is ideal for parts that are subject to high loads and require wear resistance and seizure resistance.

Recently, due to the weight reduction of automobiles and the use of front engine i-front drive (FF) systems, it has become necessary to reduce the weight of the engine, and for this reason, the cylinder □7°"' is used for A' alloy power instead of cast iron power. 1. The sea urchins are starting to turn.

In that case, cast iron cylinder liners are used in cast iron cylinders. This cylinder liner is AI! In addition to being lighter, alloys have much better thermal conductivity than cast iron, and have a larger coefficient of thermal expansion than cast iron, making the cylinder block AI! Since it is similar to an alloy, the liner and block have good adhesion even when the temperature rises, resulting in a fuel with good heat dissipation, and because the inner wall temperature of the liner can be reduced, the life of the lubricating oil can be extended, and the lubricating oil has a low viscosity. It is said that it will be possible to use lubricating oil of In addition, since the clearance is the same as that of the aluminum alloy piston material, the clearance between the piston and the piston can be set small, which is expected to reduce lubricant consumption and improve fuel efficiency.

In addition, since the AJ gold alloy has a low friction coefficient of 81, when used as a cylinder liner, it is expected to improve fuel efficiency by reducing 7 riction loss between it and the piston ring.

AI in the cylinder liner like this! Although there are many advantages to using alloys, conventionally known aluminum alloys are insufficient as cylinder liner materials for such foundries.

For example, AA standard A390.0 alloy (Si=16~1
8chi, Cu=4-5%, Mg=0.50-0.65
relationship, Fe = 0.5%, T1 = 0.2%, Zn' = O
Casting materials such as 81ch and residual HL have a wide solid-liquid coexistence temperature range, so in order to obtain a perfect casting, a large riser is required, resulting in poor yields and high costs. ,
Even with finer processing and voice-forming methods, primary Si is still coarse, so its rigidity is poor.

The fatal disadvantage of coughing is 1. When cast into a cylinder block, the material is softened by heat, which significantly reduces wear resistance, and also tends to cause chattering and cracking on the machined surface, making honing difficult. Also, in recent years, a technique has been proposed in which an alloy having a composition close to A390.0 is powdered using a powder metallurgy method and then hot extruded to form a hollow body.

(Japanese Patent Application Laid-Open No. 52-109415).

This is a method in which a hollow body is obtained by rapidly cooling a molten aluminum alloy of high St and fine particles or powder by atomizing or atomizing by centrifugal force, and extruding the same. This manufacturing method has a much better weight yield and efficiency than the hollow bodies obtained.

In addition, according to this method, the size of the crystalline St is 20 μm or less, so it has excellent ductility ± machinability, and also has high silicon AI! It also has a low coefficient of friction characteristic of alloys.

Also, by this manufacturing method, 15 to 20% Si, 1 to 5
q6 Cu, 0.5, -. 1.5%Mg, , 0
．． 5-1.5% Ni, balance AI! Hollow bodies made by extruding an alloy of , or a mixture of SiC, Sn, and graphite have been proposed.

The inventors conducted this tracing experiment and found that 20
．． OSi-4, OCu70.8 Mg −, 0,, 5,
Ni-AI! The extruded powder material with the remaining composition was used as a cylinder liner (outer diameter 7.3wn, inner diameter fi511111, height t, o5Wan,...), and A-D C-
12 alloy cylinder block (weight 3.4 kg)
As a result of a die-casting test at a molten metal temperature of 675℃, the hardness reached HR by T9 treatment before casting.
It was found that the B 80 had softened to about HRB 40 after casting. Therefore, this hollow body also becomes soft when being cast into an aluminum alloy cylinder block, and cannot be used as a cylinder liner for casting.

Casting is done by die casting or low-pressure casting, and it is desirable to make the liner as thin as possible from a cost perspective, but as the thickness becomes thinner, it becomes more difficult to transport and position the liner during casting. Since it is easily deformed by mechanical stress, it needs to have high rigidity (high hardness).

The present invention eliminates all of these drawbacks, does not soften under the heat load during casting, does not soften even in the temperature range that is applied during use, and has excellent wear resistance and seizure resistance. The purpose is to provide excellent aluminum alloy materials economically and at low cost.

The aluminum alloy powder of the present invention has a weight ratio of 51100
-300% Ni, 5.0% to 150% Ni, and if necessary CuO, 5% to 50% and Mg0.2% to 30%.
Including Chi, the rest is AI! The gist is that Si
The crystal grain size is refined to 15 μm or less, and Ni is reduced to 50 μm or less.
By containing ~15% of Ni, a Ni-containing tr intermetallic compound effective for improving high-temperature strength is precipitated.

Further, the aluminum alloy powder compact of the present invention has a weight ratio of 5i10. Consisting of O-300 parts, Ni 5.0-150 parts, and CuO, 5-50 parts and Mg as necessary.
Including 0.2~30chi, the rest is Aj? The S1 crystal grain size is 15 μm or less, and the Ni-containing intermetallic compound is finely dispersed in a size of 20 μm or less.

Furthermore, the method for manufacturing an aluminum alloy molded body of the present invention includes:
The above aluminum alloy powder is used as a raw material, and the gist is that the powder obtained by dispersing and rapidly solidifying the molten aluminum alloy is hot extruded, and the intermetallic compound phase containing Si crystal grains and Ni is The purpose of the present invention is to obtain an alloy powder compact having a fine structure.

This invention will be explained in more detail below.

First, the alloy powder of the present invention has a weight ratio of 5i10.0 to 30.
Section 0, Ni5. O~], 5.0%, further CuO, 5-5.0% and Mg0.2-3.0% as necessary
, and the balance is A7 containing unavoidable impurities, and is a heat-resistant, wear-resistant, high-strength aluminum alloy powder with a Si crystal grain size of 15 μm or less.

Generally hypereutectic Aj? It is widely known that -8t alloy has a coefficient of thermal expansion smaller than that of Aj' and has excellent heat resistance and wear resistance. In the hypereutectic Ar-St alloy casting material, St
By dispersing in the matrix as primary or eutectic crystals, it exhibits excellent high-temperature strength, wear resistance, and seizure resistance. However, since primary St 2 often crystallizes as coarse crystals, it lowers ductility and impact value and worsens machinability. Furthermore, when used for cylinder liner materials, etc., it is not suitable because it damages the mating material.

In order to solve these problems, we rapidly solidified a hypereutectic Al-Si alloy to create an alloy powder with fine primary Si crystals, and processed it into parts by extrusion molding to create a material with excellent heat resistance and wear resistance. It has been proposed to obtain the material
109415). However, heat resistance, especially high temperature strength, is still not sufficient.

The present invention is Aj! By adding 5.0 to 150% Ni to the -Si alloy, the strength and wear resistance at high temperatures are significantly improved.

Next, the reason for limiting each component in the alloy powder according to the present invention will be explained.

When the coefficient of Si is less than 10, the amount of dispersion is small and the effect on heat resistance and abrasion resistance is insufficient. In the hypoeutectic region near the 5ilO ratio, primary Si crystals cannot be crystallized and a fine eutectic structure is obtained. As the amount of Si added increases, Si primary crystals begin to crystallize, and heat resistance and wear resistance also improve.

However, when the Si content exceeds 30, coarse primary crystals of St do not disappear even as a powder by the dispersion and rapid solidification method.

When aluminum alloy powder with a coarse primary Si structure is extruded and used, it significantly deteriorates the compressibility of the powder, making it difficult to form a green compact, and it also has high deformation resistance during hot extrusion. Therefore, in addition to requiring a large extrusion force, there is also the disadvantage that the extrusion die is worn out, significantly shortening its life. In addition to these manufacturing problems, there are also the same difficulties with material properties as with cast materials, making it unsuitable as a cylinder liner material.
Crystallization of coarse primary crystals S1 must be avoided. Also,
When used as a cylinder liner by being cast into an aluminum alloy cylinder block material, the coefficient of thermal expansion decreases with the amount of Si added, and if the Si content exceeds 30, the adhesion with the cylinder block material may deteriorate.
It becomes necessary to increase the clearance with the piston.

Therefore, the amount of Si added is preferably 10.0 to 300 degrees, preferably 150 to 250 degrees.

Ni is an important component in the alloy of the present invention.

The effect of Ni addition is to improve high temperature strength and wear resistance. When Ni is added to a hypereutectic alloy, a Ni-At intermetallic compound precipitates, and in the alloy powder produced by the dispersion and rapid solidification method, which is the mainstay of the production method of the present invention, it exists as a rod-shaped structure and is easily absorbed by subsequent heat treatment. It is divided and finely dispersed in the matrix by the inter-extrusion process.

This compound is stable and difficult to grow even at high temperatures, and does not lose strength even when kept at high temperatures for a long time. Therefore, even after being exposed to high temperatures like cylinder liners for castings, the hardness does not decrease and it is possible to maintain wear resistance.

No significant effect was observed when the amount of Ni added was 5 or less, and 1
When it is 5 or more, the solubility limit of Si in the matrix becomes low, and excess Si becomes primary crystals and crystallizes in large quantities. Furthermore, the melting temperature of the alloy becomes high and oxidation of the molten metal progresses, requiring special measures to prevent oxidation, which is not economical. Furthermore, the precipitated intermetallic compounds become coarse and not only difficult to be separated by subsequent hot extrusion processing, but also impede extrudability. It was found that an unprecedented effect was exhibited when the amount of Ii added was in the range of 50 to 15.0 inches. In this way, we have developed a new method that uses the Ni-containing intermetallic compounds that precipitate by adding a large amount of Ni to improve the strength of the alloy, especially the strength at high temperatures, and improves wear resistance by fragmenting and refining these intermetallic compounds. It brings about a great effect.

The alloy powder according to the present invention is 0.5 to 5.0% as required.
of Cu and 0.2 to 3.0 mm of 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 within the solid solubility limit at the solution treatment temperature is effective in strengthening the material.

In addition, in the alloy powder of the present invention, Fe, Mn,
It is also possible to improve the high temperature strength by adding Ti, Cr, ■, Zr, Mo, Co, etc.

The reason for setting the Si crystal grain size to 15 μm or less is mainly because if the primary crystal Si size is 15 μm or more, the moldability of the subsequent alloy powder deteriorates and the material properties also deteriorate. Of course, if Si crystallizes as a eutectic, it becomes fine crystals, so no problem occurs.

The alloy powder of the present invention can be obtained by rapidly dispersing and solidifying a molten metal having the above-mentioned alloy composition using a commonly used means for producing fine powder from a molten metal, such as an atomization method or an atomization method using centrifugal force. can. The alloy powder obtained in this way has rod-shaped crystals of intermetallic compounds containing Si (crystal grains λ) and suppressed growth of Ni with a size of 15 μm or less, and is different from conventional high-Si At alloy powders. This is a new alloy powder that is not found in the 22.8Si-3, 1Cu-1, 3Mg-8, 22.8Si-3, 1Cu-1, 3Mg-8, 0Ni
-0,5Fe-AI! A micrograph of the aluminum alloy powder according to the present invention having the remaining composition is shown in FIG.

For comparison, Fig. 4 shows composition photographs of cast materials with the same composition. I 5t-3, I Cu-1,
FIG. 5 shows a photograph of the structure of alloy powder 1 (having the remaining composition of 0Mg-At).

In FIG. 3, primary crystals St exhibit a lump/shape. AI is rod-shaped! -Ni-based intermetallic compound phase.

In FIG. 4, coarse polygonal primary Si crystals are observed, and a white rod-shaped At-Ni intermetallic compound phase is observed. Fifth
The figure shows granular St primary crystals and a eutectic structure.

The alloy powder according to the present invention is suitable for hot extrusion processing, and is particularly suitable for use in high-strength aluminum alloy compacts having heat and wear resistance.

Next, the gist of the second invention of the present invention is that the alloy powder has the above-mentioned composition and the size of the Si% crystal grains is 15 μm.
or less, and the size of the intermetallic compound containing Ni is 2
This is a heat-resistant, wear-resistant, high-strength aluminum alloy powder molded body characterized by being finely dispersed to 0 μm or less.

In the present invention, the St content is set to 100 to 300% in order to improve the heat resistance, wear resistance, and seizure resistance of the molded body, and the Ni content is set to 50 to 15.0% at high temperatures. Strength,
This is to improve heat resistance and abrasion resistance.

Furthermore, by setting the size of the Si5 crystal grains to 15 μm or less, the ductility and stiffness are improved compared to conventional molded products, making machining easier and less likely to cause chattering or cracking during machining. . In addition, the fine crystals of St provide excellent wear resistance and reduce the coefficient of friction of the material, making it suitable for cylinder liners and the like.

Furthermore, by finely and uniformly dispersing the size of Ni-containing intermetallic compounds such as AJ3Ni to 5 μm or less, and even larger ones to 20 μm or less, high-temperature strength and wear resistance are significantly improved. Become. FIG. 6 shows a microscopic structure photograph of a cross section parallel to the extrusion direction of the molded article according to the present invention. In Figure 6, the dark colored part is primary Si, and the light colored part is AI! -It is eutectic with Ni-based intermetallic compounds. As seen in the figure, in the alloy compact according to the present invention, primary Si, eutectic, and intermetallic compound phases are finely distributed and uniformly distributed. A molded product having such a structure is a novel product that has not been seen in conventional molded products. For reference, FIG. 7 shows a photograph of the structure of a cross section of a high-Si aluminum alloy compact having the same composition as FIG. 5.

The aluminum alloy powder compact according to the present invention has significantly improved high-temperature strength compared to conventional products, and also has excellent wear resistance and seizure resistance. Further, since the product of the present invention has a small coefficient of friction, it is particularly suitable for parts used at high temperatures and required to have wear resistance and seizure resistance, such as cylinder liners for internal combustion engines.

The aluminum alloy powder compact according to the present invention is obtained by the method described below.

The third aspect of the present invention relates to a method for manufacturing the above-mentioned aluminum alloy powder compact, the gist of which is to disperse and rapidly solidify a molten alloy having the same composition as in the first invention. The purpose is to hot-extrude alloy powder.

The molten alloy is dispersed and rapidly solidified using Si, NiCu,
This is to form a supersaturated solid solution of alloying elements such as Mg, and to refine primary Si and intermetallic compound phases. As a method for dispersing and rapidly solidifying, known metal powder manufacturing methods such as an atomization method and a centrifugal pulverization method can be used. By using these methods to refine the powder particle size to 0.5111111 or less and rapidly solidify it, an alloy powder with a satisfactory structure can be obtained.

Next, a molded body is manufactured by hot extrusion using the alloy powder. Hot extrusion not only finishes the alloy powder into a strong compact, but also refines the crystal grains of primary Si, eutectic phase, and intermetallic phase crystallized in the alloy powder, improving the mechanical properties of the material. This is an essential requirement for

It is convenient for the work to prepare the green compact prior to hot extrusion. The green compact is produced using alloy powder at a temperature range of about 200 to 350°C. 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 N2 gas or Ar gas. Molding pressure is 05-3t
It is desirable for handling of the green compact to be carried out at approximately on/crn2 and the green compact density to be 70 inches or more as a true density ratio.

Hot extrusion is carried out at a temperature of 350°C or higher, preferably 400-400°C.
Perform in a temperature range of 70°C. This is to facilitate processing of the green compact and at the same time promote bonding between particles to make a strong compact. Furthermore, the purpose is to finely precipitate the supersaturated homolytic elements, and to divide and refine the rod-like structures of primary crystal Si 2 and intermetallic compounds, thereby improving the strength and friction characteristics of the compact. In hot extrusion, the green compact is preheated in the air or a non-oxidizing atmosphere, and then inserted into a container at approximately the same temperature for extrusion. The extrusion ratio is preferably 10 or more. If the extrusion ratio is xo"JA, voids remain in the extruded material, and the diffusion bonding between powders and the separation effect of rod-shaped intermetallic compounds are insufficient, making it impossible to obtain a material with high strength and toughness. It's for a reason.

The method of the present invention makes it possible to extremely finely and uniformly disperse the ψ deviation of Si primary crystals, eutectics, and intermetallic compound phases, making it possible to easily produce parts with particularly excellent wear resistance and friction properties. It becomes possible to obtain. Further, it is also possible to further improve the material properties by subjecting the alloy powder molded body obtained by the present invention to stabilizing heat treatment.

Next, the present invention will be explained with reference to Examples.

Example A molten high-st aluminum alloy having the composition shown in Table 1 was atomized with gas to obtain -48 mesh powder.

Next, these powders, which were preheated to a temperature of 250°C, were filled into a mold heated and maintained at the same temperature, and the powder was heated to 1,54 On/C.
Compression molded with a pressure of m2, diameter wound OO■, length 200f
A green compact of i was obtained. Next, the green compact was heated to 450°C, inserted into a container with an inner diameter of 104cm kept at the same temperature, and extruded using an indirect extrusion method (extrusion ratio 12) with a die of diameter 3 (H + 1I11). A molded article of up to -10 was obtained.

Next, all materials other than Nn9 were subjected to aging treatment at 480°C x 2 hours, water-cooled at 175°C x 10 hours, and processed into tensile test specimens with a gage distance of 50 mm and a parallel part diameter of 6 mm.
A tensile test was conducted between room temperature and 250°C. still,
The tensile test was conducted after holding for 100 hours at each test temperature. Further, the hardness was measured at the end of the chucking part of the test piece after the tensile test at each temperature. In addition, sample material No. 1
~N[L6 is a comparative example, and N[17~N[Llo is an example of the present invention. Furthermore, for comparison with cast materials, A309
．． 0 alloy mold casting material as comparison material 500℃X
A sample that had been subjected to water-cooling for 10 hours and aging at 175°C for 10 hours was also processed into the same shape and subjected to the same tensile test. The results of these tests are shown in Table-1.

As is clear from Table 1, compared to the comparative materials A390.0 alloy and Nos. 1 to 6, No. 7 according to the present invention
The molded bodies numbered 1 to 10 have high high-temperature strength and high hardness after being held at high temperatures.

Next, the hot extrusion molded body was cut, a material with a diameter of 70 mm and a thickness of 10 mm was made by hot forging, and after being machined into test pieces, a seizure resistance test, a wear resistance test, and a friction coefficient were performed. Measurements were made.

The outline of the seizure test device is schematically shown in Figs. 1 and 2, and the test device is shown schematically in Figs. 1 and 2. The oil hole (
3) Lubricating oil is applied through the A pressing force P is applied to the stator (1) with a predetermined pressure toward the right by a hydraulic device (not shown). A rotor (4) is provided opposite to the disk (2), and is configured to rotate at a predetermined speed by a drive device (not shown). Rotor (4)
A sample holder (
In 4a), a prismatic test piece (counterpart material) (5) of 5 x 5 x 1 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 3 x 2 x 3 x 3 x 2 x 2 x 2 x 2 x 2 x 2 x 2 square columnar test pieces (counterpart material) are removably arranged in two concentric circles, and the square end surface is slid against the disk (2). It can be mounted freely. In such a device, a predetermined pressing force P is applied to the stator (1) so that the disc (2) and the test piece (mate material) (5) come into contact with a predetermined surface pressure, and the oil filling hole ( 3)
Rotor (4) while lubricating the sliding surface at the specified lubricating speed.
Rotate.

The pressure acting on the stator (1) is increased stepwise at regular intervals, and the rotation of the rotor (4) causes friction between the test piece (5) and the disk (2) to cause the stator (1) to
) is applied to the load cell (7) via the spindle (6), and its change is read by the dynamic strain meter (8) and recorded by the recorder (9). Assuming that seizure occurs when the torque T increases rapidly, the contact surface pressure at that time is taken as the seizure surface pressure, and the quality of the seizure resistance is determined based on the magnitude of this.

The disk-shaped test piece (2) used for the test was heated at 300°C
The test piece (5) used was one that had been polished after being heat-treated for hr.
Two types of iron plating were applied to the 5 to 20 inch bases and polished.

As a comparison material, flake graphite cast iron used for cylinder liners was also tested.

The test conditions were a speed of 8 m/sec, lubricating oil was engine oil (SAE 20. base oil), and a temperature of 90°C.
℃ Oil amount is 3oomg/mm, contact pressure is 2akg
/ after 20 minutes break-in operation with crn2 ao kg /
cm2 for 3 minutes, then 10 kj every 3 minutes
/ cm2. The results are shown in Table-2.

As is clear from the results, the Nn7 to Nn1O material according to the present invention is superior to the combination of flake graphite cast iron (cylinder liner material) and Cr plating (piston ring surface) currently found in many gasoline engines. It shows excellent seizure resistance.

Furthermore, compared to the comparison material (casting) and SiC dispersed iron plating as seen in 11+, 1, and N [L2], when combined with hard Cr plating, the surface pressure at which seizure occurs is significantly lower. However, it is noteworthy that the difference due to the difference in the surface treatment of the mating material is reduced for M7 to Nn1O according to the present invention.

Furthermore, compared to the comparison material (casting) and Nn1.2, the surface pressure at which seizure occurs in the No. 7-1 degree molded body is higher, but this is due to AI! The large amount of hard phase dispersed in the base creates minute irregularities that act as a retainer for the oil film, and the base is dispersed and strengthened to prevent the friction surface from adhering to the mating material due to plastic flow. This is thought to be for prevention purposes.

0 Wear test and friction coefficient measurement Disc-shaped test piece (2) polished using the same testing machine used for the seizure resistance test, with hard Cr plating applied to the sliding surface of spheroidal graphite cast iron. A mating material test piece (
As 5), we conducted a test under the following conditions. The results are shown in Table-3.

(Conditions) Speed is 3'X/Bec, 5 m/Sec, 8
m/Bee at 3 levels, use engine oil (SAE20, base oil) as the lubricating oil, and set the oil temperature to 90.
℃, oil amount 500 rat/min, surface pressure 100 kg/
The sliding distance in cm2 was 500 km.

(Measurement of the amount of wear) The amount of wear on the disk-shaped test piece was measured using a surface roughness meter by running a stylus at 4 positions perpendicular to the direction of the sliding force and checking the condition of wear marks. Record on the chart. After that, the area of the concavity of the wear mark is determined and a relative comparison is made between the materials. In Table 3, the speed of the disk of flake graphite cast iron is 5 m/s.
It is expressed as a relative ratio when the cross-sectional area of the wear scar at the time of ee is set to 1.

0 The amount of wear on the mating material test piece is determined by measuring the height dimensions of four square test pieces (5) attached to the sample holder (4a) with a micrometer before and after the test, and finding the average difference. According to

The wear coefficient was calculated by reading the friction torque from the recorder (a) after traveling 200 km.

The results are shown in Table 3, and it is clear that the friction coefficient is significantly lower than that of the combination of flake graphite cast iron (cylinder liner) and Cr plating.

Furthermore, specimen M1, which was subjected to heat treatment at 300°C x 100 Hr, which corresponds to the heat load during casting, had a significant amount of wear on the disc, but No. 7 to No. 7 according to the present invention
In No. 0, the amount of wear is equal to or lower than that of flake graphite cast iron.

In addition, even if the surface treatment of the other party is hard Cr plating, S
Even with iC dispersed iron plating, there is no difference.

As described above, the alloy of the present invention is suitable for applications such as cylinder liners that are cast into A7 alloy cylinder blocks and are used in relatively high temperature ranges.

The alloy of the present invention is F e * M n * T il
Even if it contains Cr*V+Mo+Zr, Co, etc., it is thought that it contributes to heat resistance because the starting material is a powder obtained by rapid solidification.

Further, it is also possible to substitute Zn in place of Cu or Mg for the purpose of imparting age hardenability.

[Brief explanation of drawings]

1 and 2 are diagrams showing an overview of the seizing resistance testing apparatus, and FIG. 2 is a surface survey taken along the line N--N in FIG. 1. Figure 3 shows Al-22,85i-3,I according to the present invention.
Microscopic structure photograph (740x) of alloy powder having the composition of Cu-1,3Mg-8,ONi-0,5Fe. Figure 4 is a microscopic structure photograph (97x) of a cast material with the same composition as Figure 3.
. Figure 5 shows AI! −21,1, S r −3, I Cu
-Micrograph (740x magnification) of a known alloy powder with a composition of 1,0 Mg. FIG. 6 is a microscopic structure photograph of a cross section of an aluminum alloy powder compact having the same composition as FIG. 3 according to the present invention (cross section parallel to the extrusion direction, 740
times). FIG. 7 is a micrograph of a cross section of a known alloy powder compact having the same composition as FIG. 5 (cross section parallel to the extrusion direction, magnified 740 times). Patent applicant Riken Co., Ltd. Showa Denko Co., Ltd. Patent attorney Sei Kikuchi - Figure 1 Figure 2 Series 30 Army 4El (9 Fuiko vines 1)

Claims (3)

[Claims] (1) Weight ratio of 5i10.0~300chi and Ni50~
15.0% and further CuO15-50q as necessary
A heat-resistant, wear-resistant, high-strength aluminum alloy powder, characterized in that the powder is composed of Mg 6 and Mg 0.2 to 30, the remainder being A7 containing inevitable impurities, and having a Si crystal grain size of 15 μm or less. (2) Weight ratio fsi 10.0 to 30.0% and Ni5
．． 0 to 150, and if necessary CuO, 5 to 5
．． 0116 and Mg 0.2 to 3.0%, the balance being Af containing inevitable impurities, the size of the Si crystal grain is 15 μm or less, and the size of the intermetallic compound containing Ni is 20 μm or less. A heat-resistant, wear-resistant, high-strength aluminum alloy powder compact that is made of finely dispersed powder. (3) Weight ratio of 5ilO, O~300 and Ni 5
0 to 15.0%, and further Cu 05 to 15.0% as necessary
It is characterized by dispersing and rapidly solidifying a molten metal of a trh1 alloy containing 5.0% Mg, 0.2 to 30% Mg, and inevitable impurities with the remainder being quenched to form a powder, and then hot extrusion molding the obtained alloy powder. , the size of Si crystal grains is 15 μm or less,
and a method for producing a heat-resistant, wear-resistant, high-strength aluminum alloy powder compact having a structure in which Ni-containing intermetallic compounds are finely dispersed to a size of 20 μm or less.