JP6829783B2 - Manufacturing method of heat-resistant aluminum alloy material - Google Patents

Description

The present invention relates to a method for producing a heat-resistant aluminum alloy material used as a material for a turbo compressor impeller of a turbocharger as an internal combustion engine of a transportation device in an automobile or the like, and a related technique thereof.

A compressor impeller such as a compressor wheel in a turbocharger as an internal combustion engine of an automobile is required to have high strength and high rigidity at a high temperature because it is given a high speed rotation of over 10,000 rpm under a high temperature condition of about 150 ° C. .. In addition, the compressor impeller is required to be lightweight in order to reduce energy loss, and is also required to have strength capable of withstanding high-speed rotation.

For example, conventionally, the compressor impeller is a 2618 alloy (Cu: 1.9% by mass to 2.7% by mass, Mg: 1.3% by mass to 1.8% by mass, Ni: 0.9% by mass to 1.2). Mass%, Fe: 0.9% by mass to 1.3% by mass, Si: 0.1% by mass to 0.25% by mass, Ti: 0.04% by mass to 0.1% by mass, Al: balance) It was manufactured by cutting cast and forged products with an alloy composition. However, with the recent increase in the speed of cutting, the extruded aluminum alloy material has been made into a cut product, and it has become necessary to further improve the machinability and the high temperature strength.

For example, Patent Document 1 below discloses a technique for providing an extruded Al—Cu—Mg-based aluminum alloy having higher strength at a high temperature of 160 ° C. than before.

Patent No. 5284935

However, in the technical field of internal combustion engines such as automobiles, compressor impellers are required to rotate at higher speeds, and aluminum alloy materials capable of withstanding a further rise in operating temperature are currently required.

An object of the present invention is to provide a method for producing a heat-resistant aluminum alloy material which can sufficiently withstand high-temperature use and has excellent high-temperature strength, and related techniques thereof.

In order to achieve the above object, the gist of the present invention is as follows.

[1] Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0. 5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: less than 0.3% by mass, Ti: 0 .06% by mass, balance: Al and unavoidable impurities The alloy composition of the continuous cast material is heat-treated and then plastically processed to increase the aluminum crystal grain length by the cross-linking method to 250 μm to 2000 μm. A method for producing a heat-resistant aluminum alloy material, which comprises obtaining an adjusted heat-resistant aluminum alloy material.

[2] The method for producing a heat-resistant aluminum alloy material according to item 1 above, wherein a heat-resistant aluminum alloy material is obtained by cutting the plastic processed material obtained by the plastic working.

[3] The method for producing a heat-resistant aluminum alloy material according to item 2 above, wherein the plastic working material is heat-treated before being cut.

[4] As the heat treatment, solution treatment, quenching treatment, and aging treatment are sequentially performed, while the heat treatment is performed.
In the solution treatment, it is heated at a temperature of 485 ° C to 530 ° C for 0.5 hours to 6 hours, in the quenching treatment, it is cooled with water at 10 ° C to 90 ° C, and in the aging treatment, it is cooled at 170 ° C to 230 ° C for 1 hour to 20. The method for producing a heat-resistant aluminum alloy material according to item 3 above, which is heated for an hour.

[5] The method for producing a heat-resistant aluminum alloy material according to any one of the above items 1 to 4, wherein the processing rate in the axial direction in the plastic working is 20% to 80%.

[6] The method for producing a heat-resistant aluminum alloy material according to any one of items 1 to 5 above, wherein the plastic working is a stationary working that compresses in the axial direction.

[7] The method for producing a heat-resistant aluminum alloy material according to any one of items 1 to 6 above, wherein the plastic working is mold forging.

[8] Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0. 5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: less than 0.3% by mass, Ti: 0 .06% by mass, balance: Al and unavoidable impurities A continuous cast material having an alloy composition is heat-treated and then plastically processed to obtain a plastically processed material.
A method for manufacturing a compressor impeller, characterized in that a compressor impeller whose aluminum crystal grain length is adjusted to 250 μm to 2000 μm by the line of intersection method is obtained by cutting the plastic work material.

[9] Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0. 5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: less than 0.3% by mass, Ti: 0 .06% by mass, balance: obtained by heat treatment and plastic processing on a continuous cast material having an alloy composition of Al and unavoidable impurities, and the aluminum crystal grain length adjusted by the crossing method to 250 μm to 2000 μm. Aluminum alloy material for compressor impeller, which is characterized by being

[10] Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0. 5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: less than 0.3% by mass, Ti: 0 .06% by mass, balance: obtained by heat treatment and die forging of a continuous cast material having an alloy composition of Al and unavoidable impurities, and the aluminum crystal grain length adjusted by the crossing method to 250 μm to 2000 μm. Forged material for compressor impeller, which is characterized by being

[11] Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0. 5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: less than 0.3% by mass, Ti: 0 .06% by mass, balance: obtained by heat treatment, die forging and cutting of a continuous cast material having an alloy composition of Al and unavoidable impurities, and the aluminum crystal grain length by the crossing method is 250 μm to 2000 μm. A compressor impeller characterized by being tuned.

According to the method for producing a heat-resistant aluminum alloy material according to the invention [1], it is possible to obtain a heat-resistant aluminum alloy material that can sufficiently withstand high-temperature use, has excellent high-temperature strength, and is suitable as a material for a compressor impeller. it can.

According to the method for producing a heat-resistant aluminum alloy material according to the inventions [2] to [7], the above effect can be obtained more reliably.

According to the method for manufacturing a compressor impeller according to the invention [8], it is possible to obtain a compressor impeller that can sufficiently withstand high temperature use and has excellent high temperature strength.

According to the aluminum alloy material for a compressor impeller of the present invention [9], it can sufficiently withstand high temperature use and has excellent high temperature strength.

According to the forged material for a compressor impeller of the present invention [10], it can sufficiently withstand high temperature use and has excellent high temperature strength.

According to the compressor impeller of the invention [11], it can sufficiently withstand high temperature use and has excellent high temperature strength.

FIG. 1 is a perspective view showing a test material adopted in Examples and Comparative Examples, FIG. 1A is a perspective view showing a test material obtained by the manufacturing method 1, and FIG. 1B is a manufacturing method. It is a perspective view which shows the test material obtained by 2-5. FIG. 2 is a diagram for explaining the positional relationship of the test piece with respect to the test material of Examples and Comparative Examples, and FIG. 2A-1 is a diagram for explaining the positional relationship of the test piece with respect to the test material according to the manufacturing method 1. FIG. 2A-2 is a side view for explaining the positional relationship of the test piece with respect to the test material according to the manufacturing method 1, and FIG. (B-1) is a side view for explaining the positional relationship of the test piece with respect to the test material according to the manufacturing method 1. The perspective view and FIG. (B-2) for explaining the positional relationship of the test piece with respect to the test piece are side views for explaining the positional relationship of the test piece with respect to the test material according to the manufacturing methods 2 to 4. FIG. 3 is a diagram for explaining the positional relationship of the JIS No. 4 test piece with respect to the test material of Examples and Comparative Examples, and FIG. 3 (a-1) is a diagram of the JIS No. 4 test piece with respect to the test material according to the manufacturing method 1. A perspective view for explaining the positional relationship, FIG. (a-2) is a plan view for explaining the positional relationship of the JIS No. 4 test piece with respect to the test material according to the manufacturing method 1, and FIG. (B-1) is a manufacturing method 2. The perspective view for explaining the positional relationship of the JIS No. 4 test piece with respect to the test material according to 4 and FIG. 4 (b-2) is for explaining the positional relationship of the JIS No. 4 test piece with respect to the test material according to the manufacturing methods 2 to 4. It is a plan view of.

Next, a method for manufacturing a compressor impeller related to the present invention will be described in detail.

The compressor impeller of the present invention is made of a heat-resistant aluminum alloy material made of an Al—Cu—Mg-based alloy.

The heat-resistant aluminum alloy material of the present invention has Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, and Ni: 0.6% by mass to 2.6% by mass. Mass%, Fe: 0.5% by mass to 1.5% by mass, Mn: 0.1% by mass to 0.4% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: 0.3 It has an alloy composition of less than mass%, Ti: less than 0.06 mass%, balance: Al and unavoidable impurities.

In the above alloy composition, Cu is an element that needs to be added in order to improve the normal temperature strength and the high temperature strength. If the Cu content is less than 3.0% by mass, the effect of sufficiently improving the strength cannot be obtained, which is not preferable. Further, when the Cu content exceeds 5.5% by mass, the strength becomes saturated, and addition of more than that is meaningless. Therefore, the Cu content needs to be 3.0% by mass to 5.5% by mass, preferably 3.2% by mass to 4.7% by mass.

Like Cu, Mg is an element that needs to be added to improve normal temperature strength and high temperature strength. If the Mg content is less than 1.1% by mass, the effect of sufficiently improving the strength cannot be obtained, which is not preferable. Further, if the Mg content exceeds 2.5% by mass, plastic workability such as forging workability and castability deteriorate, which is not preferable. Therefore, the Mg content needs to be 1.1% by mass to 2.5% by mass.

Ni is an element added to improve normal temperature strength and high temperature strength. If the Ni content is less than 0.6% by mass, the effect of sufficiently improving the strength cannot be obtained, which is not preferable. Further, if the Ni content exceeds 2.6% by mass, it binds to Cu in the alloy to form crystallization, and conversely, the strength decreases, which is not preferable. Therefore, the Ni content is set to 0.6% by mass to 2.6% by mass.

Fe is an element added to improve high temperature strength. If the Fe content is less than 0.5% by mass, the effect of sufficiently improving the strength cannot be obtained, which is not preferable. On the other hand, if the Fe content exceeds 1.5% by mass, giant crystallization is generated, and conversely, the strength is lowered, which is not preferable. Therefore, the Fe content needs to be 0.5% by mass to 1.5% by mass, preferably 0.8% by mass to 1.2% by mass.

Mn is an element added to improve high temperature strength. If the Mn content is less than 0.1% by mass, the effect of sufficiently improving the strength cannot be obtained, which is not preferable. On the other hand, if the Mn content exceeds 0.4% by mass, huge crystallization is generated, and conversely, the strength is lowered, which is not preferable. Therefore, the Mn content needs to be 0.1% by mass to 0.4% by mass, preferably 0.2% by mass to 0.35% by mass.

Zr is an element added to suppress recrystallization of a plastically deformed continuous cast material (continuous cast material) and to improve the strength from room temperature to high temperature. If the Zr content is less than 0.01% by mass, the effect cannot be sufficiently obtained, which is not preferable. Further, if the Zr content exceeds 0.3% by mass, huge crystallization is generated and the strength is lowered, which is not preferable. Therefore, the content of Zr needs to be 0.01% by mass to 0.3% by mass, preferably 0.1% by mass to 0.25% by mass.

Si produces Mg and an intermetallic compound Mg2Si, which coarsens as it continues to be used at high temperatures, which may result in a particularly low high temperature strength. Therefore, in the present invention, by limiting the content of Si as an additive element or an unavoidable impurity to less than 0.3% by mass (including 0% by mass), the formation of Mg2Si itself is suppressed and Mg2Si is coarsened due to high temperature use. It is possible to prevent a decrease in high temperature strength and fatigue strength (high temperature instability). The Si content is preferably 0.1% by mass or less.

Ti is an element that refines the crystal grains of the ingot structure to stabilize the mechanical properties. However, in the present invention, the grain boundaries at the time of high temperature deformation are formed by positively coarsening the crystal grains without making them finer. I try to suppress slippage. Therefore, in the present invention, it is necessary to limit the Ti content to less than 0.06% by mass (including 0% by mass). That is, by limiting the Ti content in this way, the formation of Al3Ti can be avoided, the refinement of crystal grains can be prevented, and sufficient high-temperature strength can be reliably obtained. In particular, when the Ti content is limited to less than 0.04% by mass in the present invention, the crystal grain length can be reliably adjusted within the specified range described later.

By the way, various unavoidable impurity elements are contained in the aluminum alloy obtained in the actual operation. The Al—Cu—Mg-based aluminum alloy material according to the present invention also contains unavoidable impurity elements that are almost the same as those of the JIS2000-based aluminum alloy, but has no particular adverse effect. Specifically, in the alloy composition of the aluminum alloy material of the present invention, Cr and Zn are individually less than 0.05% by mass, Pb, Bi and Sn are individually less than 0.01% by mass, and other elements are individually. If it is less than 0.05% by mass and the total unavoidable impurities excluding Si is less than 0.15% by mass, no particular problem occurs.

In the present invention, for example, a continuous cast material (billet) having the above alloy composition is produced by melting by a well-known method, the continuous cast material is heat-treated, and further plastic working such as forging is performed. Thereby, a heat-resistant aluminum alloy material for a compressor impeller related to the present invention can be obtained.

The heat treatment is a solution treatment, a quenching treatment, and an aging treatment, and the continuous cast material is treated in this order.

In the solution treatment, the heating temperature is preferably 485 ° C. to 530 ° C., and the treatment time is preferably 0.5 hours (hr) to 6 hours.

In the quenching process, it is preferable to quench with water at 10 ° C to 90 ° C.

In the aging treatment, the heating time is preferably 170 ° C. to 230 ° C., and the treatment time is preferably 1 hour to 20 hours.

The aluminum alloy continuous cast material heat-treated in this way is cut to an appropriate size to obtain a material for plastic working (forging material), and then plastic working is performed on the material. In the present invention, as the plastic working, forging processing such as stationary processing and mold forging is carried out.

For example, the forged material formed by performing mold forging on the forged material is configured as the forged material for the compressor impeller of the present invention.

Further, in the plastic working of the present invention, it is preferable to set the machining rate (installation rate) in the axial direction to 20% to 80%. By setting this processing rate within the above-mentioned specified range, sufficient normal temperature strength and high temperature strength can be surely obtained. In other words, if the processing rate deviates from the above-mentioned specified range, it may not be possible to reliably obtain sufficient normal temperature strength and high temperature strength.

Further, in the forged material (plastic working material) of the present invention, it is necessary to adjust the aluminum crystal grain length to 250 μm to 2000 μm by the line of intersection method. That is, if the crystal grain length is less than 250 μm, it may not be able to withstand high temperature use due to creep deformation, and sufficient high temperature strength may not be obtained. If the crystal grain length exceeds 2000 μm, it may be cold. It is not preferable because the formability in plastic working such as interforging may decrease.

In the present invention, a compressor impeller such as a compressor wheel of a turbocharger is manufactured by cutting the forged material for the compressor impeller described above.

The forged material for the compressor impeller of the present invention manufactured as described above is excellent in normal temperature strength, high temperature strength, and rigidity, and in particular, the strength in the radial direction (LT direction) orthogonal to the axial direction (L direction). Will be higher. Therefore, if a compressor impeller such as a compressor wheel of a turbocharger is manufactured using this forged material, the overall room temperature strength (normal temperature strength) and high temperature strength are excellent, and at the same time, the dynamic balance at high speed rotation is excellent. Moreover, a compressor impeller that has the optimum performance for each part according to different required characteristics and desired characteristics, especially the strength and rigidity of the blade part, especially the strength and rigidity of the tip of the blade part (chip edge part). Obtainable. Specifically, it is possible to obtain a compressor impeller that can withstand high-temperature use at about 170 ° C. due to high-speed rotation and has excellent heat resistance.

As described above, according to the manufacturing method of the present invention, a heat-resistant aluminum alloy material and a forged material for a compressor impeller having the above-mentioned excellent performance, and a compressor impeller can be manufactured.

Hereinafter, examples related to the present invention and comparative examples to be compared with the examples will be described in detail.

As shown in Table 1, two types of alloys having an alloy composition of A type and B type were prepared. As for the alloy composition itself, both the A type alloy and the B type alloy are included in the gist of the present invention, but the B type alloy has a smaller Ti content than the A type alloy. Is limited to.

<Examples 1 to 5>
As shown in Table 2, an aluminum alloy having a B-type alloy composition was cast into a rod shape having a diameter of φ50 mm, and further soaked at 470 ° C. × 7 hr to obtain a continuous cast material.

A method of obtaining a cut product by cutting a continuously cast rod having a B-type alloy composition to a predetermined length is defined as a manufacturing method 1, and the length L in the axial direction is as shown in FIG. 1A by this manufacturing method 1. A columnar test material (test material before heat treatment) W of Example 1 having a (thickness) T of 50 mm was produced.

Further, as shown in Table 2, a method of obtaining a hot-installed forged product by hot-installing forging in the axial direction L at a processing rate of 25% with respect to the cut product obtained by the manufacturing method 1 is obtained. As shown in FIG. 1 (b), the drum-shaped test material (test material before heat treatment) W of Example 2 having a thickness T of 37.5 mm was manufactured by this manufacturing method 2.

Further, as shown in Table 2, the cut product obtained by the manufacturing method 1 is subjected to hot stationary forging in the axial direction at a processing rate of 50%, 75%, and 90% to obtain a hot stationary forged product. The methods were set to manufacturing methods 3 to 5, respectively, and as shown in FIG. 1 (b) according to each manufacturing method 3 to 5, the drum-shaped test material of Examples 3 to 5 having a thickness T of 25 mm, 12.5 mm, and 5 mm. (Test material before heat treatment) W was produced respectively.

<Comparative Examples 1 to 5>
As shown in Table 2, a continuous cast material was obtained in the same manner as in the above Examples using an aluminum alloy having an A type alloy composition. Cylindrical or drum-shaped test materials of Comparative Examples 1 to 5 (supplied before heat treatment) by applying the same manufacturing methods 1 to 5 as in the above examples to the continuously cast rod having the A type alloy composition. (Test material) W was manufactured respectively.

<Heat treatment>
Next, the test materials before heat treatment of Examples 1 to 5 and Comparative Examples 1 to 5 obtained in the production methods 1 to 5 were subjected to a solution treatment by heating at 510 ° C. for 3 hours, and then with water at 80 ° C. Quenching treatment for quenching was performed, and further aging treatment was performed by heating at 200 ° C. for 10 hours to produce test materials W (test materials after heat treatment) of Examples 1 to 5 and Comparative Examples 1 to 5, respectively.

The crystal grain length, room temperature tensile strength, and high temperature tensile strength of the heat-treated test materials W of Examples 1 to 4 and Comparative Examples 1 to 4 thus obtained were measured as follows. The results are also shown in Table 2. The test material W of Example 5 and Comparative Example 5 is not suitable for practical use because the processing rate (installation rate) is as high as 90% and the yield of the raw material is poor. For this practical reason, the following measurements were not performed on the test material W of Example 5 and Comparative Example 5.

<Measurement of crystal grain length>
2 (a-1) and 2 (a-2) are diagrams for explaining the positional relationship of the test piece S1 with respect to the test material W according to the manufacturing method 1, and FIGS. 2 (b-1) and 2 (b-2) are manufacturing methods. It is a figure for demonstrating the positional relationship of the test piece S1 with respect to the test material W by 2-4. As shown in these figures, each of the test materials W of Examples 1 to 4 and Comparative Examples 1 to 4 is cut into a 15 mm square from the central portion in the axial direction L and the radial direction (LT direction orthogonal to the axial direction L). Each test piece S1 having a dice shape (cubic shape) of Examples 1 to 4 and Comparative Examples 1 to 4 was obtained. Further, after each of these test pieces S1 was polished and electrolytically etched, a microscope image of the sample surface was obtained by a polarizing microscope having a magnification of 25 times, with the plane perpendicular to the axial direction L as the observation plane.

Image analysis was performed on the microscopic images of the test pieces S1 of Examples 1 to 4 and Comparative Examples 1 to 4 thus obtained, and the crystals constituting the metal structure of each test piece S1 according to the cutting method specified in JIS G0551. The average grain length was calculated. The crystal grain length is perpendicular to the axial direction X.

<Measurement of room temperature tensile strength>
3 (a-1) and 3 (a-2) are views for explaining the positional relationship of the JIS No. 4 test piece S2 with respect to the test material W according to the manufacturing method 1, and FIGS. 3 (b-1) and 3 (b-2) are shown. It is a figure for demonstrating the positional relationship of JIS No. 4 test piece S2 with respect to the test material W by manufacturing method 2-4. As shown in these figures, JIS No. 4 test piece S2 extending along the radial direction is cut out from the axial center of the test material W, and each JIS No. 4 test piece S3 is in accordance with the provisions of JIS Z2241. A tensile test was performed at room temperature to measure the tensile strength.

<Measurement of tensile strength at 150 ° C>
Similar to the measurement of the room temperature tensile strength, the JIS No. 4 test piece S2 (see FIG. 3) cut out from the test material W was held at 150 ° C. for 100 hr, and then the tensile test was performed at the same temperature in accordance with the JIS Z2241 regulations. And the tensile strength was measured.

<Measurement of tensile strength at 170 ° C)
Similar to the measurement of the room temperature tensile strength, the JIS No. 4 test piece S3 (see FIG. 3) cut out from the test material W was held at 170 ° C. for 100 hr, and then the tensile test was performed at the same temperature in accordance with the JIS Z2241 regulations. And the tensile strength was measured.

<Evaluation>
As is clear from Table 2, the test pieces of Comparative Examples 1 to 4 had crystal grain lengths of less than 250 μm, which deviated from the specified range of the present invention. Therefore, those of Comparative Examples 1 to 4 cannot withstand high temperature use due to creep deformation, and it is considered that the high temperature strength may decrease.

On the other hand, the test pieces of Examples 1 to 4 have crystal grain lengths of 250 μm or more, which are included in the gist of the present invention. Therefore, since creep deformation can be suppressed, it can be judged that it can withstand high temperature use and can secure sufficient high temperature and high strength. Therefore, the aluminum alloy material of the examples related to the present invention is particularly excellent in normal temperature strength and high temperature strength, and is therefore suitable as a material for a compressor impeller.

Further, as described above, Example 5 and Comparative Example 5 having a processing rate of 90% are considered to be unsuitable for practical use because the yield of the raw material is poor.

The production method of the present invention can be suitably used when producing a heat-resistant aluminum alloy material used as a material for a compressor impeller.

L: Axial direction

Claims (7)

Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0.5% by mass ~ 1.5% by mass, Mn: 0.1% by mass to 0.40% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: 0.1% by mass or less, Ti: 0.06% by mass %, Remaining mass: A continuous cast material having an alloy composition of Al and unavoidable impurities was soaked and then plastically processed to adjust the aluminum crystal grain length by the crossing method to 250 μm to 2000 μm. A heat-resistant aluminum alloy material shall be obtained.
A method for producing a heat-resistant aluminum alloy material, wherein the machining rate in the axial direction in the plastic working is 50% to 80%. The method for producing a heat-resistant aluminum alloy material according to claim 1, wherein a heat-resistant aluminum alloy material is obtained by cutting the plastic processed material obtained by the plastic working. The method for producing a heat-resistant aluminum alloy material according to claim 2, wherein the plastically worked material is heat-treated before being cut. As the heat treatment, solution treatment, quenching treatment and aging treatment are sequentially performed, while
In the solution treatment, it is heated at a temperature of 485 ° C to 530 ° C for 0.5 hours to 6 hours, in the quenching treatment, it is cooled with water at 10 ° C to 90 ° C, and in the aging treatment, it is cooled at 170 ° C to 230 ° C for 1 hour to 20. The method for producing a heat-resistant aluminum alloy material according to claim 3, wherein the material is heated for an hour. The method for producing a heat-resistant aluminum alloy material according to any one of claims 1 to 4, wherein the plastic working is a stationary working that compresses in the axial direction. The method for producing a heat-resistant aluminum alloy material according to any one of claims 1 to 5, wherein the plastic working is mold forging. Cu: 3.0% by mass to 5.5% by mass, Mg: 1.1% by mass to 2.5% by mass, Ni: 0.6% by mass to 2.6% by mass, Fe: 0.5% by mass ~ 1.5% by mass, Mn: 0.1% by mass to 0.40% by mass, Zr: 0.01% by mass to 0.3% by mass, Si: 0.1% by mass or less, Ti: 0.06% by mass %, Remaining mass: A continuous cast material having an alloy composition of Al and unavoidable impurities is soaked and then plastically processed to obtain a plastically processed material.
By cutting the plastic working material, it is assumed that a compressor impeller whose aluminum crystal grain length is adjusted to 250 μm to 2000 μm by the line of intersection method is obtained.
A method for manufacturing a compressor impeller, characterized in that the machining rate in the axial direction in the plastic working is 50% to 80%.

Images