JPH08176768A - Wear resistant aluminum member and production thereof - Google Patents

Abstract

PURPOSE: To provide wear resistant aluminum members (material, parts, etc.) having excellent workability and excellent wear resistance and mechanical properties. CONSTITUTION: The wear resistant aluminum members are produced by stages of subjecting a hypereutectic aluminum-silicon based alloy blank contg., by weight%, 12 to 25% silicon, 0.5 to 5.0% copper, 0.1 to 2.0% magnesium, 0.003 to 0.020% phosphorus and consisting of the balance aluminum and other necessary elements including manganese, iron, nickel, zinc, chromium, titanium, tin, etc., with impurities to strong plastic working corresponding to rolling of a draft of >=50% to crush the silicon of primary crystals, then subjecting te blank to structure control by heating up to a solid-liquid co-existence temp. to impart a solid phase rate of 0.3 to 0.7.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a wear-resistant aluminum member (including a material itself and parts (products) using the material) having a hard primary silicon with a controlled metallographic structure, and a method for manufacturing the same. It has good workability, excellent wear resistance and mechanical properties, and is suitable for automobile parts, agricultural machine parts,
The present invention relates to a wear resistant aluminum member which is preferably used as a material for industrial machine parts and the like, and a method for manufacturing the same.

[0002]

2. Description of the Related Art Attempts to optimize primary silicon in hypereutectic aluminum-silicon wear-resistant alloys from the viewpoint of wear resistance and workability have been made for a long time. In the known alloys other than casting, for example, a method is known in which powder is used as a raw material and sintering / plastic working or a composite process thereof is performed.

[0003]

However, the range of the structure control by these methods is limited, and in the cast alloy, the grain size of the primary crystal is 1 although it is inexpensive.
There is a problem that it is difficult to control the particle diameter to 0 μm or less, and the grain size of silicon is roughly determined by the casting method. Further, even in the method using powder as a raw material, there is a problem that the material cost becomes high.

That is, in the prior art, what is a technique for obtaining a member (material, component, etc.) that simultaneously satisfies both the conditions of being inexpensive and the condition that the particle size distribution of silicon is arbitrarily controlled? In reality, the wear resistance of the wear resistant aluminum alloy is limited or limited.

[0005]

SUMMARY OF THE INVENTION The present invention is intended to solve the problems of the conventional method, and it is inexpensive.
A wear-resistant aluminum member (material, which can satisfy both of the conditions that the particle size distribution of silicon is controlled arbitrarily) at the same time and has excellent workability as well as wear resistance and mechanical properties The purpose is to provide parts, etc.).

[0006]

As described in claim 1, the wear-resistant aluminum member according to the present invention is made of a hypereutectic aluminum-silicon alloy as a raw material, and its structure can be controlled at a solid-liquid coexisting temperature. The feature is that it is done.

Further, in the method for producing a wear-resistant aluminum member according to the present invention, as described in claim 2, a step of controlling the microstructure by setting the hypereutectic aluminum-silicon alloy material to a solid-liquid coexisting temperature. It is characterized by having to go through.

In an embodiment of the method for producing a wear resistant aluminum member according to the present invention, as described in claim 3, the hypereutectic aluminum-silicon alloy material is not subjected to strong plastic working until it is subjected to strong plastic working. After crushing the crystalline silicon, the temperature may be raised to the solid-liquid coexistence temperature to control the structure, and as described in claim 4, the rolling reduction is performed as the strong plastic working. Of 50% or more is processed (including plastic working with a working rate of 50% or more in forging, extrusion, upsetting, etc.) to crush the primary crystal silicon, and then the solid-liquid coexisting temperature As solid phase ratio of 0.
The temperature can be raised to a temperature range giving 3 to 0.7 to control the structure.

In an embodiment of the wear resistant aluminum member and the method for producing the same according to the present invention, as described in claim 5, the hypereutectic aluminum-silicon alloy is, by weight%, silicon: 12 to 12. 25%, copper: 0.5-5.
0%, magnesium: 0.1 to 2.0%, phosphorus: 0.00
3 to 0.020%, and the balance may be aluminum and other necessary elements such as manganese, iron, nickel, zinc, chromium, titanium, tin, and impurities.

Further, in the embodiment of the wear resistant aluminum member and the manufacturing method thereof according to the present invention, JIS
As the one corresponding to ADC14 aluminum alloy,
As described in claim 6, hypereutectic aluminum-
Silicon-based alloys are, by weight, silicon: 16-18%, copper:
4.0 to 5.0%, magnesium: 0.45 to 1.65
%, Manganese: 0.5% or less, phosphorus: 0.003 to 0.0
20%, iron: 1.3% or less, zinc: 1.5% or less, and the balance may be aluminum and impurities.

Similarly, in the embodiment of the wear resistant aluminum member and the manufacturing method thereof according to the present invention, the JI
As the one corresponding to S AC9B aluminum alloy,
As described in claim 7, hypereutectic aluminum-
The silicon-based alloy is, by weight, silicon: 18 to 20%, copper:
0.5-1.5%, magnesium: 0.5-1.5%,
Manganese: 0.5% or less, phosphorus: 0.003 to 0.020
%, Iron: 0.8% or less, zinc: 0.2% or less, and nickel: 0.5 to 1.5% in some cases, with the balance being aluminum and impurities.

Similarly, in the embodiment of the wear resistant aluminum member and the manufacturing method thereof according to the present invention, the JI
As the one corresponding to S AC9A aluminum alloy,
As described in claim 8, hypereutectic aluminum-
The silicon-based alloy is, by weight, silicon: 22 to 24%, copper:
0.5-1.5%, magnesium: 0.5-1.5%,
Manganese: 0.5% or less, phosphorus: 0.003 to 0.020
%, Iron: 0.8% or less, zinc: 0.2% or less, and nickel: 0.5 to 1.5% in some cases, with the balance being aluminum and impurities.

Similarly, in the embodiment of the wear-resistant aluminum member and the method for producing the same according to the present invention, the hypereutectic aluminum alloy having a silicon content of 16% or less and not established in either JIS ADC or AC. As described in claim 9, the hypereutectic aluminum-silicon alloy has a silicon content of 1% by weight.
4-16%, copper: 2.0-5.0%, magnesium:
0.1-1.0%, manganese: 0.3-0.8%, chromium: 0.1-0.3%, titanium: 0.05-0.20
%, Phosphorus: 0.003 to 0.020%, iron: 1.5% or less, and in some cases, calcium: less than 0.005%, the balance being aluminum and impurities. it can.

[0014]

As described in claim 1, the wear-resistant aluminum member according to the present invention is made of a hypereutectic aluminum-silicon alloy as a raw material, and its structure is controlled at a solid-liquid coexisting temperature. Therefore, the particle size distribution of silicon is controlled by an inexpensive means, the matrix structure other than silicon is fine, and the workability is improved without using an expensive means of pulverization. It is excellent and has excellent mechanical properties such as wear resistance and toughness.

The method for producing a wear-resistant aluminum member according to the present invention, as described in claim 2, includes a step of controlling the microstructure of a hypereutectic aluminum-silicon alloy material at a solid-liquid coexisting temperature. Therefore, the particle size distribution of silicon is controlled by an inexpensive method, and the matrix structure other than silicon is fine, and it is possible to process without using the expensive method of pulverization. A wear-resistant aluminum member having good wear resistance and mechanical properties such as wear resistance and toughness is manufactured.

In an embodiment of the method for producing a wear-resistant aluminum member according to the present invention, as described in claim 3, the hypereutectic aluminum-silicon alloy material is first subjected to strong plastic working before being subjected to strong plastic working. After crushing the crystalline silicon, the temperature was raised to the solid-liquid coexistence temperature to control the structure, so that the inexpensive particles will be fine-grained and uniformly distributed. At the same time, since the matrix structure other than silicon is a fine-grained structure, a wear-resistant aluminum member having good workability and excellent mechanical properties such as wear resistance and toughness can be manufactured.

Further, in the embodiment of the method for producing a wear-resistant aluminum member according to the present invention, as described in claim 4, the processing corresponding to rolling with a rolling reduction of 50% or more as the strong plastic working ( After forging, extruding, upsetting, and other plastic working with a working rate of 50% or more) to crush the primary crystal silicon, the solid-liquid coexistence temperature is set to a solid-phase rate of 0.3 to 0.7. The temperature can be raised to a given temperature range for tissue control. That is, as described in claim 3, first, the hypereutectic aluminum-silicon alloy material is subjected to a strong plastic working to sufficiently crush the primary crystal silicon, and then the solid-liquid coexistence temperature is raised. The step of heating and controlling the structure is carried out, and this strong plastic working may be carried out by any method as long as sufficient crushing of primary silicon is obtained, but according to claim 4, As described above, if the process corresponds to rolling with a rolling reduction of 50% or more, the subsequent heat treatment can obtain a state sufficient to obtain fine-grained silicon.

After that, by maintaining this material at a predetermined temperature within the solid-liquid coexistence temperature range, not only the base aluminum alloy structure but also the fine graining of the primary crystal silicon is achieved. It is thought that this is because the solute concentration distribution due to the interfacial energy, which is the driving force for solute redistribution, is sufficient, and the mass transfer by diffusion through the liquid phase is significantly faster than in the solid state. To be

At this time, if the solid fraction exceeds 0.7, the primary silicon tends to be unable to be sufficiently changed into particles, and if the solid fraction is less than 0.3, the sample melts during holding. The protrusion tends to be remarkable, and the original shape may not be maintained. Therefore, it is desirable that the predetermined temperature within the solid-liquid coexistence temperature range is a temperature at which the solid phase ratio is between 0.3 and 0.7.

Thus, first, hypereutectic aluminum-
Different from the conventional silicon-dispersed wear-resistant aluminum alloy technology by crushing primary silicon of silicon-based alloy material sufficiently by severe plastic working and then maintaining this material at a predetermined temperature within the solid-liquid coexistence temperature range. A wear resistant member (material, component, etc.) of a hypereutectic aluminum-silicon alloy in which any fine granular silicon is uniformly distributed can be obtained.

The wear-resistant aluminum member thus obtained satisfies not only the condition that it is light in weight but also that it is inexpensive, and the condition that the silicon grain distribution is arbitrarily controlled. Abrasion resistant aluminum −
It is a silicon alloy member, and the present invention provides a technique that overcomes the limits and limitations of wear resistance of the prior art.

In an embodiment of the wear-resistant aluminum member and the method for producing the same according to the present invention, as described in claim 5, the hypereutectic aluminum-silicon alloy is, by weight%, silicon: 12 to 12. 25%, copper: 0.5-5.
0%, magnesium: 0.1 to 2.0%, phosphorus: 0.00
3 to 0.020% with the balance being aluminum and other necessary elements such as manganese, iron, nickel, zinc, chromium, titanium, tin, etc. and impurities. The action of each basic additive element constituting the aluminum member and the reason for limiting the composition range will be shown.

Silicon: Silicon (Si) is an element that contributes to the improvement of wear resistance, and primary crystal Si that contributes to the improvement of wear resistance.
When the Si content is less than 12%, crystallization does not occur, so 12% was made the lower limit. However, if it exceeds 25%, the liquidus temperature of the alloy element rises, the melting and casting properties deteriorate, and the machinability deteriorates significantly.

Copper: Copper (Cu) is an element that contributes to the improvement of room temperature and high temperature strength by solid solution strengthening and age hardening. However, if it is less than 0.5%, its effect is small, and if it exceeds 5.0%, the toughness is lowered and shrinkage cavities are often generated, so the range is made 0.5 to 5.0%.

Magnesium: Magnesium (Mg) is an element that contributes to the improvement of strength by age hardening due to coexistence with silicon. However, if it is less than 0.1%, the effect is small, and if it exceeds 2.0%, the toughness decreases, so
The range was 0.1 to 2.0%.

Phosphorus: Phosphorus (P) is a primary crystal Si crystallized during casting.
Is an element that contributes to the miniaturization of. However, 0.0
If it is less than 03%, the effect is small, and if it exceeds 0.020%, the castability such as the flow of molten metal tends to deteriorate, so that
The range was 003 to 0.020%.

Aluminum: Aluminum (Al) contributes to the weight reduction of castings and can meet the requirements for weight reduction of castings, so manganese, iron, nickel, zinc, chromium, titanium, tin, etc. And the other necessary elements and impurities as the balance.

The hypereutectic aluminum-silicon alloy according to claim 5 of the present invention has the above-mentioned chemical composition, but in a further specific embodiment, a hypereutectic crystal as shown below is used. It can be an aluminum-silicon alloy.

The hypereutectic aluminum-silicon alloy according to claim 6 corresponds to the JIS ADC14 alloy, and in weight%, silicon: 16-18%, copper: 4.0-.
5.0%, magnesium: 0.45 to 1.65%, manganese: 0.5% or less, phosphorus: 0.003 to 0.020%,
Iron: 1.3% or less, zinc: 1.5% or less, and the balance consisting of aluminum and impurities.
The workability of the S ADC14 alloy and the mechanical properties such as wear resistance and toughness are further improved.

The hypereutectic aluminum-silicon alloy according to claim 7 corresponds to the JIS AC9B alloy, and in weight%, silicon: 18-20%, copper: 0.5-.
1.5%, magnesium: 0.5 to 1.5%, manganese: 0.5% or less, phosphorus: 0.003 to 0.020%,
Iron: 0.8% or less, zinc: 0.2% or less, and the balance consisting of aluminum and impurities.
The workability of the SAC9B alloy and the mechanical properties such as wear resistance and toughness are further improved.

The hypereutectic aluminum-silicon alloy according to claim 8 corresponds to the JIS AC9A alloy, and in weight%, silicon: 22-24%, copper: 0.5-.
1.5%, magnesium: 0.5 to 1.5%, manganese: 0.5% or less, phosphorus: 0.003 to 0.020%,
Iron: 0.8% or less, zinc: 0.2% or less, and the balance consisting of aluminum and impurities.
The S AC9A alloy has further improved workability and mechanical properties such as wear resistance and toughness.

The hypereutectic aluminum-silicon alloy according to claim 9 has a silicon content of 16% or less and JIS
It corresponds to a hypereutectic aluminum alloy that has not been established in either ADC or AC, and in weight%, silicon: 14 to 16%, copper: 2.0 to 5.0%, magnesium: 0. 1 to 1.0%, manganese: 0.3 to 0.8%,
Chromium: 0.1-0.3%, Titanium: 0.05-0.2
0%, phosphorus: 0.003 to 0.020%, iron: 1.5% or less, and in some cases calcium: 0.005%
And a balance of aluminum and impurities, the hypereutectic aluminum alloy having a silicon content of 16% or less and further improved mechanical properties such as wear resistance and toughness. Become.

[0033]

Example As a test material, a material having a chemical composition shown in Table 1 was used. Here, Examples 1 to 4 and Reference Examples 1 to 3 are J
The composition is equivalent to IS ADC14. Further, Examples 5 and 6 have compositions corresponding to JIS AC9B and 9A, respectively. Furthermore, Example 7 has a silicon content of J
The composition of the hypereutectic aluminum alloy is 16% or less, which is less than that of IS ADC14. These were cast into a boat-shaped mold to obtain an ingot of about 500 g each. At this time, the size of the primary crystal silicon was about 35 μm to 60 μm, although the size of the material having a large amount of silicon was larger.

[0034]

[Table 1]

On the other hand, in advance, an experiment for determining the relationship between the temperature and the solid fraction in the solid-liquid coexisting temperature range of the test material and thermal analysis were performed to determine the holding temperature in the solid-liquid coexisting temperature range. As a result, 575 ° C., 567 ° C., 560 ° C., 556 ° C. and 550 ° C. in the test materials of Examples 1 to 4 and Reference Examples 1 to 3 have solid fractions of 0.1 or less, 0.3, and 550 ° C., respectively.
Corresponding to 0.6, 0.7 and 0.85. In addition, the solid phase ratio is 0.6 at 575 ° C. in the test materials of Examples 5 and 6.
give. Further, the sample material of Example 7 also has a solid fraction of 0.6 at 565 ° C. The holding time at those temperatures was unified to 30 minutes.

First, the effect of plastic working on the crushing of silicon particles was investigated. In this case, the plastic working includes casting,
Although extrusion, upsetting, rolling and the like can be adopted, rolling is adopted in this embodiment. The results are shown in Table 2.

[0037]

[Table 2]

In Examples 2 and 4 and Reference Example 3, all the isothermal holding except for Reference Example 3 was carried out in the state where the solid fraction was 0.6, but the difference was due to the strength of plastic working by rolling. There is. In Example 2, the rolling reduction was 60%. In this case, as shown in Table 2, the large primary crystal silicon was finely crushed, and after the subsequent isothermal holding, an ideal structure having fine granular and uniform silicon particles was obtained. Was obtained. This microstructure is shown in FIG.

As shown in FIG. 1, the aluminum alloy portion of the matrix is also in the form of fine particles having a grain size of 50 μm or less.
The silicon particles are also large, about 10 μm, and most of them are in the form of fine particles of uniform micron order. The particles of silicon or intermetallic compound surrounding the alpha phase are also extremely small.

In Example 4 in which the rolling reduction was 50%, the silicon remained partially in the central portion as it was before rolling, but as is clear from Table 2, many of the silicon were crushed and the solid fraction was 0. .6
By maintaining the same temperature at the solid-liquid coexisting temperature, the structure similar to that in Example 2 could be obtained.

On the other hand, in Reference Example 3 in which the rolling reduction was 40%, most of the silicon remained before rolling, and as shown in Table 2, only the silicon near the surface was crushed. . Therefore, it was not possible to expect the effect of improving the structure by keeping the isothermal condition in the solid-liquid coexisting temperature range thereafter, so the experiment was stopped at that point.

From these results, in order to obtain fine granular silicon in the subsequent isothermal holding process in the solid-liquid coexisting temperature range,
It was found that at least the plastic working equal to or more than the plastic working corresponding to the rolling with the rolling reduction of 50% is required. All subsequent experiments were performed at a reduction rate of 60%.

In each of Examples 1 to 3 and Reference Examples 1 and 2, rolling was performed at a rolling reduction of 60%, and then the results were obtained when the material was kept isothermally at a temperature at which various solid fractions were provided. here,
Good results are obtained when the solid phase ratio is 0.3 to 0.
This was the case of Examples 1 to 3 held during the period up to 7.

Then, the solid fraction becomes 0.1 or less 575
In Reference Example 1 in which the sample was kept isothermally at 0 ° C., although the shape was slightly maintained, the sample material could not maintain the shape well and was largely deformed so as to collapse. This tendency was slightly observed in Example 1 in which the solid phase ratio was 0.3, but only a few liquid-phase sweat-like projections appeared on the surface of the test material, and there was no particular problem.

On the contrary, Reference Example 2 shows the case where the solid phase ratio is kept at 550 ° C., which is as large as 0.85. Crystalline silicon remained almost unchanged when it was crushed.

From these experiments, it was confirmed that by holding the hypereutectic aluminum-silicon alloy material, in which the primary silicon was sufficiently crushed, in the solid phase ratio between 0.3 and 0.7, the problem of deformation was observed. It is clear that a hypereutectic aluminum-silicon alloy member (materials, parts, etc.) in which fine-grained silicon particles are uniformly dispersed and the aluminum alloy portion of the base itself is also fine-grained is obtained. It was

Further, the above-mentioned effect is obtained by hypereutectic aluminum-
Experiments of Examples 5 to 7 were conducted in order to confirm that they are commonly expressed in silicon-based alloy materials. In each of the examples, the rolling reduction during rolling was 60%, and the solid fraction at the isothermal holding temperature was 0.6. In this case, since the amount of silicon largely fluctuated from about 15% (Example 7) to 23% (Example 6), the amount of silicon particles was different, but the obtained microstructure was different from that of Example 2. Almost the same, the silicon particles were fine and evenly distributed. From this result, it can be said that the effect of the present invention is generally obtained with the hypereutectic aluminum-silicon alloy.

As described above, according to the present invention, it is possible to obtain a material or a component in which fine granular silicon particles are uniformly dispersed without following the expensive step of pulverization. Further, it is possible to obtain fine granular silicon of the order of micron which cannot be obtained by the conventional cast alloy.

As one of the wear modes of the hypereutectic aluminum-silicon alloy, a mechanism in which large silicon particles are damaged during friction, and the silicon particles that fall off at that time become abrasive grains to promote wear on the contrary. However, in the material or component according to the present invention, the silicon particles are finely distributed, and the silicon distributed in the fine particles is less likely to be crushed during friction, and is unlikely to cause the unstable friction state as described above. Has become.

Therefore, the material or component (ie member) according to the present invention exhibits stable and good wear resistance as compared with other materials having the same chemical composition. The fact that the number of crushed silicon particles is extremely small compared to other materials even in the surface state obtained by ordinary processing also leads to the advantageous direction of the wear resistance of the member of the present invention.

[0051]

As described in claim 1, the wear-resistant aluminum member according to the present invention is made of a hypereutectic aluminum-silicon alloy as a raw material, and its structure is controlled at a solid-liquid coexisting temperature. Therefore, the particle size distribution of silicon can be controlled by an inexpensive means and the matrix structure other than silicon can be made fine, and the workability can be improved without using an expensive means of pulverization. It is possible to provide a wear resistant aluminum member which is good and has excellent mechanical properties such as wear resistance and toughness, which is a remarkably excellent effect.

The method for producing a wear-resistant aluminum member according to the present invention, as described in claim 2, includes the step of controlling the microstructure of a hypereutectic aluminum-silicon alloy material at a solid-liquid coexisting temperature. Therefore, it is possible to control the particle size distribution of silicon by an inexpensive method and to make the matrix structure other than silicon fine, and to process it without using the expensive method of powdering. It is possible to produce a wear-resistant aluminum member which has excellent wear resistance and mechanical properties such as wear resistance and toughness.

In an embodiment of the method for producing a wear-resistant aluminum member according to the present invention, as described in claim 3, the hypereutectic aluminum-silicon alloy material is not subjected to strong plastic working until After crushing the crystalline silicon, the temperature is raised to the solid-liquid coexistence temperature to control the structure, so an inexpensive method can be used to make the silicon particles fine and evenly distributed. At the same time, since the matrix structure other than silicon can be made into a fine grain structure, it becomes possible to manufacture a wear-resistant aluminum member which has good workability and excellent mechanical properties such as wear resistance and toughness.

Therefore, since a member in which the silicon particles are arbitrarily uniformly distributed in a fine granular form and the base aluminum alloy is also in a fine shape, the aluminum member obtained by the present invention has excellent workability. It is possible to provide an inexpensive material / rough material having stable and good wear resistance and also excellent in mechanical properties.

The silicon in the hypereutectic aluminum-silicon alloy member obtained by the present invention is in the form of fine particles of the order of microns, and the silicon in the member once in this microstructure state is subjected to subsequent plastic working and mechanical processing. It is extremely unlikely to be crushed during processing. Therefore, this material can be post-processed by extremely general mechanical processing including plastic working such as forging, rolling, extrusion, upsetting, etc., and chemical corrosion / electrochemical treatment for creating an ideal friction surface state. There is no need for special surface processing or special processing tools like.

Therefore, it is possible to widen the range in which it can be used in the ordinary machined surface state,
Even in this process, the technique is cheaper than the conventional wear-resistant aluminum alloy member.

In addition, recently, several member manufacturing techniques for pushing an alloy into a mold in a solid-liquid coexistence temperature range have appeared.
It is also possible to press the material into the mold at a temperature in the solid-liquid coexistence temperature range during or after the process of maintaining the solid-liquid coexistence temperature range of the process according to the present invention. In this case, the tendency of granulation of the structure becomes more remarkable than in the case of only isothermal holding, and it has been confirmed that the member according to the present invention is more suitable for such a construction method.

Further, in the member according to the present invention, the matrix structure other than the primary crystal silicon portion is also finely grained, that is, the alpha phase is also finely grained, and the silicon in the eutectic portion surrounding it is also extremely fine. Since it is granular, it is clear that such a microstructure does not have a brittle notch-shaped portion and has good mechanical properties, and the member (material, component, etc.) according to the present invention is generally In terms of excellent mechanical properties, it has a great effect that it is superior to conventional materials.

More specifically, as described in claim 4, after performing a process corresponding to rolling with a reduction rate of 50% or more as a strong plastic working to crush the primary crystal silicon, By increasing the solid-liquid coexistence temperature to a temperature range that gives a solid phase ratio of 0.3 to 0.7 to control the structure, excellent workability, wear resistance, and mechanical properties as described above are achieved. A wear resistant aluminum member will be manufactured.

Further, as described in claim 5, the hypereutectic aluminum-silicon alloy is, by weight%, silicon: 1
2 to 25%, copper: 0.5 to 5.0%, magnesium:
0.1 to 2.0%, phosphorus: 0.003 to 0.020%, and the balance aluminum and other necessary elements such as manganese, iron, nickel, zinc, chromium, titanium, tin, etc. and impurities By this, a hypereutectic aluminum-silicon alloy for casting or die casting, which is excellent in workability, wear resistance and mechanical properties, can be provided.

The hypereutectic aluminum-silicon alloy according to claim 6 corresponds to the JIS ADC14 alloy, and in weight%, silicon: 16-18%, copper:
4.0 to 5.0%, magnesium: 0.45 to 1.65
%, Manganese: 0.5% or less, phosphorus: 0.003 to 0.0
20%, iron: 1.3% or less, zinc: 1.5% or less, and the balance consisting of aluminum and impurities, and the workability of JIS ADC14 alloy and mechanical properties such as wear resistance and toughness. Can be further improved.

Further, the hypereutectic aluminum-silicon alloy according to claim 7 corresponds to the JIS AC9B alloy, and in weight%, silicon: 18 to 20%, copper: 0.
5 to 1.5%, magnesium: 0.5 to 1.5%, manganese: 0.5% or less, phosphorus: 0.003 to 0.020%,
Iron: 0.8% or less, zinc: 0.2% or less, and the balance consisting of aluminum and impurities.
It is possible that the S AC9B alloy has further improved workability and mechanical properties such as wear resistance and toughness.

Furthermore, the hypereutectic aluminum-silicon alloy according to claim 8 corresponds to the JIS AC9A alloy, and in% by weight, silicon: 22-24%, copper:
0.5-1.5%, magnesium: 0.5-1.5%,
Manganese: 0.5% or less, phosphorus: 0.003 to 0.020
%, Iron: 0.8% or less, zinc: 0.2% or less,
The balance consists of aluminum and impurities,
It is possible that the JIS AC9A alloy has further improved workability and mechanical properties such as wear resistance and toughness.

Furthermore, the hypereutectic aluminum-silicon alloy according to claim 9 is a hypereutectic aluminum alloy which has a silicon content of 16% or less and is not established in either JIS ADC or AC. Corresponding, by weight%, silicon: 14-16%, copper: 2.0-5.0%,
Magnesium: 0.1-1.0%, Manganese: 0.3-
0.8%, chrome: 0.1-0.3%, titanium: 0.0
5 to 0.20%, phosphorus: 0.003 to 0.020%, iron:
Contains up to 1.5%, optionally calcium:
Restricted to less than 0.005%, the balance consisting of aluminum and impurities, further improving the workability and mechanical properties such as wear resistance and toughness of a hypereutectic aluminum alloy with a silicon content of 16% or less. It has the excellent effect that it can be

[Brief description of drawings]

FIG. 1 is a copy of a metallographic micrograph showing the microstructure of an abrasion resistant aluminum member of Example 2 of the present invention.

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[Procedure amendment]

[Submission date] December 22, 1994

[Procedure Amendment 1]

[Document name to be amended] Statement

[Name of item to be corrected] Figure 1

[Correction method] Change

[Correction content]

FIG. 1 is a metallographic micrograph showing a microstructure of Example 2 of the present invention.

[Procedure Amendment 2]

[Document name to be corrected] Drawing

[Correction target item name] 1

[Correction method] Change

[Correction content]

FIG.

Claims (9)

[Claims] 1. A wear-resistant aluminum member characterized by comprising a hypereutectic aluminum-silicon alloy as a raw material, and having its structure controlled at a solid-liquid coexisting temperature. 2. A method for producing a wear-resistant aluminum member, which comprises the step of controlling the structure of a hypereutectic aluminum-silicon alloy material at a solid-liquid coexisting temperature. 3. A hypereutectic aluminum-silicon alloy material is subjected to severe plastic working to crush primary silicon, and then the temperature is raised to a solid-liquid coexistence temperature to control the structure. A method for producing the wear-resistant aluminum member described above. 4. Severe plastic working, which corresponds to rolling with a rolling reduction of 50% or more, is performed to crush the primary crystal silicon, and then a solid-liquid coexistence temperature of a solid-phase ratio of 0.3 to 0.7 is given. The method for producing a wear-resistant aluminum member according to claim 3, wherein the structure is controlled by raising the temperature to a temperature range. 5. The hypereutectic aluminum-silicon alloy is, by weight, silicon: 12 to 25%, copper: 0.5 to 5.0%,
Magnesium: 0.1 to 2.0%, Phosphorus: 0.003 to
The wear-resistant aluminum member according to any one of claims 1 to 4, wherein 0.020% is contained, and the balance is aluminum and other necessary elements and impurities. 6. The hypereutectic aluminum-silicon alloy is, by weight%, silicon: 16-18%, copper: 4.0-5.0%,
Magnesium: 0.45 to 1.65%, manganese: 0.
5% or less, phosphorus: 0.003 to 0.020%, iron: 1.3
%, Zinc: 1.5% or less, and the balance consisting of aluminum and impurities, the wear-resistant aluminum member according to claim 5, and a method for producing the same. 7. The hypereutectic aluminum-silicon alloy is, by weight, silicon: 18 to 20%, copper: 0.5 to 1.5%,
Magnesium: 0.5-1.5%, Manganese: 0.5%
The wear-resistant aluminum member according to claim 5, further comprising phosphorus: 0.003 to 0.020%, iron: 0.8% or less, zinc: 0.2% or less, and the balance being aluminum and impurities. The manufacturing method. 8. The hypereutectic aluminum-silicon alloy is, by weight, silicon: 22 to 24%, copper: 0.5 to 1.5%,
Magnesium: 0.5-1.5%, Manganese: 0.5%
The wear-resistant aluminum member according to claim 5, further comprising phosphorus: 0.003 to 0.020%, iron: 0.8% or less, zinc: 0.2% or less, and the balance being aluminum and impurities. The manufacturing method. 9. The hypereutectic aluminum-silicon alloy is, by weight%, silicon: 14 to 16%, copper: 2.0 to 5.0%,
Magnesium: 0.1-1.0%, Manganese: 0.3-
0.8%, chrome: 0.1-0.3%, titanium: 0.0
5 to 0.20%, phosphorus: 0.003 to 0.020%, iron:
Contains up to 1.5%, optionally calcium:
The wear-resistant aluminum member according to claim 5, which is regulated to less than 0.005%, and the balance comprises aluminum and impurities, and a method for producing the same.