JPH11140603A - Wear resistant sintered alloy material for part of compressor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain a sintered alloy material excellent in wear resistance and applicable to severe operational conditions by forming its structure into the mixed one of the primary phase essentially consisting of Fe, and in which fine carbides are precipitated and the secondary phase essentially consisting of Fe and softer than the primary phase and specifying the area ratio of the primary phase the secondary phase. SOLUTION: It is composed of a ferrous sintered alloy material having a mixed structure of the primary phase essentially consisting of Fe, and in which fine carbides are precipitated and the secondary phase essentially consisting of Fe and softer than the primary phase. The primary phase is composed of one or more kinds selected from, by weight, <=2.0% C, <=17% Cr, <=12% Mo, <=20% W, <=6% V, <=3% Ti, <=3% Nb, <=3% B and >=13% Co, and the balance Fe, has fine carbides of' <=10 μm and has hardness of >=400 Hv. The area ratio in the ferrous matrix structure is regulated to 30 to 95%. The secondary phase has either compsn. of carbon steel or low alloy steel, and the area ratio in the matrix structure is regulated to 5 to 70%.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

The present invention relates to a compressor vane,
The present invention relates to a sintered alloy material for a compressor component such as a scroll stopper ring, and particularly to a sintered alloy material for a compressor component having excellent wear resistance.

[0002]

2. Description of the Related Art A sintered alloy is obtained by compounding and kneading an alloy powder, filling a mold, compression-molding, and then sintering at a predetermined temperature atmosphere. Can be easily manufactured, and functions can be easily combined.
Parts with unique functions can be manufactured. Further, it is suitable for manufacturing porous materials and difficult-to-process materials, and for manufacturing mechanical parts having complicated shapes. In recent years, this sintered alloy has been applied to a sliding member such as a vane of a compressor that requires wear resistance.

[0003] In recent years, the conditions of use of compressors used in freezers and refrigerators, air conditioners, and the like have become increasingly severe. Due to environmental problems such as destruction of the ozone layer, a change from a conventionally used refrigerant containing chlorine in the molecule to a refrigerant not containing chlorine in the molecule has been studied. However, a refrigerant containing no chlorine has poor lubrication performance, and there has been a demand for an improvement in wear resistance of a sliding material such as a vane of a compressor.

On the other hand, as a sintered alloy for a compressor vane,
A chromium-containing iron-based sintered alloy having a mixed structure of a phase in which Cr carbide is precipitated and a Fe-C-based martensite phase is used. In this iron-based sintered alloy containing chromium,
For compressor vanes, wear resistance may be insufficient, and models used are limited to those with low output.
As a measure to improve the wear resistance of the compressor vane, for example, JP-A-7-293463 discloses that a compound layer composed of iron, chromium, and nitrogen is formed on the surface of an iron-based sintered alloy containing chromium. A method of applying a ceramic coating of chromium nitride, titanium nitride or titanium carbide has been proposed. However, when such a compound layer is formed or a ceramic coating is applied, there is a problem that a manufacturing process is complicated and a manufacturing cost is increased.
Therefore, a sintered alloy having excellent wear resistance has been demanded as a material for a compressor vane which can be applied to any type of compressor and has high wear resistance.

[0005]

DISCLOSURE OF THE INVENTION The present invention advantageously solves the above-mentioned problems and has excellent wear resistance and is suitable for compressor parts such as compressor vanes and scroll stopper rings. The purpose of the present invention is to propose a system-based sintered alloy material.

[0006]

SUMMARY OF THE INVENTION The present invention is directed to a mixed structure of a first phase mainly composed of Fe in which fine carbides are precipitated and a second phase mainly composed of Fe and softer than the first phase. An iron-based sintered alloy material mainly comprising an iron-based matrix structure, wherein the first phase contains, by weight, C: 2.0% or less, Cr: 17% or less, Mo: 12% or less, W: : 20% or less, V: 6% or less, Ti:
3% or less, Nb: 3% or less, B: 3% or less, Co: 13% or less selected from the group consisting of Fe and unavoidable impurities, and fine particles of 10 μm or less Carbide precipitates, has a hardness of 400 Hv or more, the area ratio in the iron-based matrix is 30 to 95%, and the second phase is any one of carbon steel and low alloy steel. An iron-based sintered alloy material for compressor parts having excellent wear resistance, having the above composition and having an area ratio in the iron-based matrix structure of 5 to 70%.

In the present invention, the second phase may be pure iron containing C: 0.5% or less by weight, or C: 1.5%.
%, Mn: 0.5% or less, Si: 1.0% or less
Carbon steel consisting of Fe and unavoidable impurities, or C:
Contains 1.5% or less, Mn: 0.5% or less, Si: 1.0% or less
Cr: 4% or less, Mo: 3% or less, Ni: 5% or less, V: 1.0
% Or less, Cu: 5.0% or less, one or two selected from
It is preferably made of any one of low alloy steels containing at least one species and the balance being Fe and unavoidable impurities.

Further, in the present invention, in addition to the above-mentioned iron-based matrix structure, an infiltrated or previously added Cu phase or Cu alloy phase may be contained in an area ratio of 1 to 20%. In addition to the base tissue, average particle size: 20-100 μm, hardness: 70
Hard particles of 0 to 1500 Hv may be dispersed in an area ratio of 1 to 20%. The hard particles are Fe-Mo particles, Fe-W particles, Cr-
Any of Mo-Co intermetallic compound particles and C-Cr-W-Co particles is preferable.

In the present invention, a solid lubricant may be contained in an area ratio of 0.5 to 10% in addition to the iron-based matrix structure, and the solid lubricant may be graphite, sulfide, nitride, Any of the fluorides is preferred. Further, in the sintered alloy material of the present invention, the sintered pores may be infiltrated with a low melting point metal. The low melting point metal is Pb, Pb alloy, Sn, Sn
Metals selected from alloys, Zn, and Zn alloys are preferred.

[0010]

BEST MODE FOR CARRYING OUT THE INVENTION An iron-based sintered alloy material according to the present invention has an area ratio of 30 to 95%, a first phase mainly composed of Fe in which fine carbides are precipitated, and an area ratio of 5 to 70%. The main structure is an iron-based matrix having a mixed structure of Fe and a second phase that is softer than the first phase. The first phase precipitates fine carbides of 10 μm or less and has a hardness of 400 Hv or more. When the size of the precipitated fine carbide exceeds 10 μm, the strength decreases,
Increases opponent's aggression If the hardness is less than 400 Hv, the wear resistance cannot be improved. The size of the fine carbide is 1
The hardness of the first phase is preferably 450 to 900 Hv from the viewpoints of abrasion resistance, strength, and aggressiveness to a partner. Note that the structure of the first phase is basically a structure in which fine carbides are precipitated.

The ratio of the first phase in the iron-based matrix is 30 to 95% by area. If it is less than 30%, the wear resistance deteriorates, and the object of the present invention cannot be achieved. On the other hand, if it exceeds 95%, the improvement in wear resistance is saturated, and the effect is small compared to the increase in the amount of alloy elements, which is economically disadvantageous. The ratio of the first phase in the iron-based matrix is preferably 50 to 90%. First
The composition of the phase contains, by weight, C: 2.0% or less, and Cr: 17%.
%, Mo: 12% or less, W: 20% or less, V: 6% or less,
Ti: 3% or less, Nb: 3% or less, B: 3% or less, Co: 13%
One or two or more selected from the following and the balance
It is preferably composed of Fe and inevitable impurities.

Hereinafter, the reasons for limiting the preferred component composition of the first phase will be described. C: 2.0% or less C is an element necessary for adjusting a phase to a predetermined structure and hardness, or for further forming a carbide.
If it exceeds 2.0%, the melting point is lowered and a liquid phase is formed, resulting in liquid phase sintering, resulting in an excessive amount of carbide precipitation, an increase in the number of voids, deterioration of elongation characteristics, and a decrease in dimensional accuracy. C is preferably set to 0.5% or more. If it is less than 0.5%, sintering does not proceed, the amount of carbide precipitation is small, and the wear resistance deteriorates. More preferably, it is 0.7 to 1.7%.

One or more selected from Cr, Mo, W, V, Ti, Nb, B, and Co can be contained. Cr: 17% or less Cr is an element that increases the strength, heat resistance and wear resistance. However, if it exceeds 17%, the amount of precipitated Cr carbides becomes excessive and the machinability decreases, and the carbides precipitated in the phase Is 10 μm
It is difficult to become the following fine carbides. Cr is preferably at least 4%. If it is less than 4%, the precipitation amount of Cr carbide is small and the wear resistance is slightly reduced. More preferably, it is 4 to 12%.

Mo: not more than 12% Mo is precipitated as a solid solution and carbide to increase the hardness of the phase,
Although the abrasion resistance is improved, if it exceeds 12%, the fluidity of the powder decreases and the formability deteriorates. Mo is preferably at least 3%. If it is less than 3%, the amount of precipitated carbide is small, and the wear resistance is deteriorated. More preferably, it is 3 to 6%.

W: not more than 20% W is an element that forms carbides and improves wear resistance. If it exceeds 20%, the amount of carbides precipitated becomes excessive, the strength becomes too high and the elongation is insufficient. W is preferably 4% or more. If it is less than 4%, the amount of carbide precipitation is small, and the wear resistance is slightly reduced. It is more preferably 4 to 12%, and still more preferably 4 to 7%.

V: 6% or less V is an element which forms carbides and improves wear resistance. If V exceeds 6%, the amount of carbides precipitated becomes excessive, the strength becomes too high and the elongation is insufficient. V is preferably 1% or more. If it is less than 1%, the amount of carbide precipitation is small, and the wear resistance is slightly reduced. It is more preferably 2 to 5%, and still more preferably 2 to 3%.

Ti: 3% or less Ti is an element that forms carbides and improves wear resistance. However, if it exceeds 3%, the amount of precipitation is too large and elongation is insufficient. Note that Ti is preferably 0.5 to 2.0%. Nb: 3% or less Nb is an element that forms carbides and improves abrasion resistance like Ti, but if it exceeds 3%, the amount of precipitation is too large and elongation is insufficient. Incidentally, Nb is preferably 0.5 to 2.0%.

B: 3% or less B is an element which improves the wear resistance by setting the base structure to a predetermined structure together with the carbide forming element. If it exceeds 3%, coarse precipitates are formed and wear resistance is deteriorated.
B is preferably 0.5 to 2.0%. Co: 13% or less Co is an element that increases the high-temperature strength and improves the wear resistance by suppressing the strength reduction with the temperature rise. However, when the content exceeds 13%, the effect is saturated, and the addition amount is increased. Is not economically effective,
Co is limited to 13% or less. In addition, it is preferably in the range of 8 to 10%.

The balance of the first phase is substantially Fe. Next, the second phase will be described. In the sintered alloy material of the present invention, the second phase is formed in order to improve the compaction property. The second phase may be softer than the first phase, and may be 400
The hardness is preferably Hv or less. The presence of the second phase in the iron-based matrix structure significantly improves the strength and toughness of the sintered body as compared with the case of the hard phase alone. Also, the first
The amount of alloying elements is smaller than the phase, which is advantageous in cost. The composition is preferably made of any of pure iron, carbon steel and low alloy steel containing Fe as a main component.

The ratio of the second phase in the iron-based matrix is 5 to 70% by area. If it is less than 5%, the compaction property is insufficient, and if it exceeds 70%, the wear resistance is adversely affected. For this reason, the ratio of the second phase in the iron-based base was limited to 5 to 70%. The composition of the second phase contains, by weight, C: 0.5% or less, pure iron comprising Fe and unavoidable impurities, or C: 1.5% or less, Mn: 0.5% or less, Si: 1.0% or less. Carbon steel containing the balance of Fe and unavoidable impurities, or C: 1.5% or less, Mn: 0.5% or less, Si: 1.0% or less, Cr: 4% or less, Mo: 3% or less, Ni: 5% or less , Cu: 5.0% or less, V: 1.0% or less, and preferably one of low alloy steels containing one or more kinds and the balance being Fe and unavoidable impurities.

The selection of the second phase can be appropriately selected depending on the purpose of use of the sintered alloy material. In order to make the composition of the second phase softer than that of the first phase, it is preferable to use pure iron containing C: 0.5% or less and comprising Fe and inevitable impurities. C: 0.5
%, It tends to be harder than the first phase, so the upper limit was set for pure iron. When hardness is required, alloying elements can be added to achieve a desired hardness. In the present invention, the amount of alloying element added to the second phase is limited to a relatively small amount as described above for the purpose.

If the hardness of the second phase needs to be higher than that of pure iron, it is preferable to use carbon steel. The composition of carbon steel is as follows: C: 1.5% or less, Mn: 0.5% or less, Si: 1.0%
It is preferable to contain the following and make the balance Fe and inevitable impurities. If the content of C exceeds 1.5%, the liquid phase is liable to come out. If the content of Mn exceeds 0.5%, the sintering diffusivity decreases. , The respective upper limits were set.

Further, when the hardness of the second phase is required to be high, it is preferable to use a low alloy steel obtained by adding an alloying element to the carbon steel. Alloying elements: Cr: 4% or less, Mo: 3
%, Ni: 5% or less, Cu: 5.0% or less, V: 1.0% or less. All of these alloying elements are elements that can increase the hardness of steel, with 4% for Cr, 3% for Mo, 5% for Ni, and 5.5% for Cu.
If 0% and V exceed 1.0%, the hardness is excessively increased and becomes equal to that of the first phase.

The sintered alloy material of the present invention may contain a Cu phase or a Cu alloy phase in an area ratio of 1 to 20% in addition to the iron-based matrix structure described above. Cu powder or Cu alloy powder may be mixed with iron powder and added.In addition, when powder is mixed, Cu powder or Cu alloy powder is not added, but on powder compact during sintering or on sintered body during heat treatment. Cu or Cu alloy may be loaded and Cu or Cu alloy may be infiltrated into the sintered hole.

The Cu phase or Cu alloy phase precipitates in the matrix structure, thereby improving the thermal conductivity and the interparticle bonding force of the sintered body. Further, the elongation characteristics and machinability are improved by further depositing in the pores and sealing. Cu phase or Cu
If the alloy phase is less than 1%, elongation is reduced and workability of the sintered body is reduced. On the other hand, the Cu phase or Cu
Since the alloy phase becomes coarse, the shear strength and wear resistance of the sintered body decrease. Therefore, Cu phase or Cu alloy phase is 1-20%
Limited to the range.

In the present invention, instead of the above-described sealing treatment with Cu or a Cu alloy, the sintered pores may be infiltrated with a low melting point metal. Pb, Pb alloy, S
n, Sn alloy, Zn, and Zn alloy are preferred. The sintered pores infiltrated by the low melting point metal are preferably in the range of 1 to 20% in area ratio. If it is less than 1%, the elongation of the sintered body decreases, and
If it exceeds, the strength of the sintered body decreases.

In the sintered alloy material of the present invention, in addition to the iron-based matrix, hard particles having an average particle diameter of 20 to 100 μm and a hardness of 700 to 1500 Hv are added in an area ratio of 1 to 20%. They may be dispersed. Hard particles can be expected to have the effect of improving the wear resistance of the sintered alloy.However, if the average particle size is less than 20 μm, the particles easily diffuse during sintering, and the effect of improving the wear resistance is small.
If it exceeds 100 μm, the machinability is adversely affected. Therefore, the average particle size of the hard particles is set in the range of 20 to 100 μm. If the hardness of the hard particles is less than 700 Hv, the effect of improving the wear resistance is small, and if the hardness exceeds 1500 Hv, the machinability is adversely affected. Therefore, the hardness of the hard particles is set in the range of 700 to 1500 Hv.

The hard particles are dispersed in an area ratio of 1 to 20%.
If it is less than 1%, the effect of improving the wear resistance is small, and if it exceeds 20%, the machinability and the compactability deteriorate, so that the dispersion amount of the hard particles is in the range of 1 to 20%. In the present invention, the hard particles may be any of Fe-Mo particles, Fe-W particles, Cr-Mo-Co intermetallic compound particles, and C-Cr-W-Co particles.

The Fe-Mo particles and Fe-W particles are dispersed in the matrix by adding them as ferromolybdenum or ferrotungsten powder. The composition of ferromolybdenum is
A composition within the range specified in JIS is sufficient. The composition of ferromolybdenum is, for example, Mo: 50 to 70 wt%, Fe:
The composition of ferrotungsten is, for example, W: 40 to 60 wt% and Fe: 40 to 60 wt%.

The Cr—Mo—Co intermetallic compound particles are Cr: 10 wt.
%, Mo: 30 wt%, and Co: 60 wt%. Further, C-Cr-W-Co particles are as follows: C: 1 to 5 wt%, Cr: 40 to 70 wt%, W: 10 to 30 wt%
%, Co: 5-20 wt%. In the present invention, a solid lubricant can be added in addition to the above-mentioned iron-based matrix structure in order to improve machinability, wear resistance, and anti-partition attack resistance. Solid lubricant has an area ratio of 0.
It is desirable to contain 5 to 10%. If it is less than 0.5%, the effect cannot be expected, while if it exceeds 10%, the progress of the sintering reaction is hindered, and the mechanical properties deteriorate. As the solid lubricant, any one of graphite, sulfide, nitride, and fluoride is preferable. The sulfide, MnS, MoS _2, and examples of the fluoride CaF ₂ are suitable.

In order to obtain the sintered alloy material of the present invention, one or more selected from the group consisting of Cr, Mo, W, V, Ti, Nb, B and Co as the first phase are contained. An alloy steel powder having a composition of the balance of Fe and a steel powder having a second phase of pure iron, carbon steel, or a low alloy steel composition, or further, a Cu powder or a Cu alloy powder are kneaded. In addition, you may mix zinc stearate etc. as a lubricant.

Further, a solid lubricant or ferromolybdenum powder which becomes hard particles may be added and blended. Next, these powders are filled in a mold, and compressed and molded by a molding press to obtain a green compact. Next, the green compact is sintered to obtain a sintered body. In the present invention, the green compact is preferably heated and sintered in a protective atmosphere at a temperature of 1100 to 1200 ° C. If the temperature is lower than 1100 ° C., the sintering diffusion is insufficient.

Further, the sintered body may be loaded with Cu or Cu alloy or a low-melting-point metal and heated to perform a sealing treatment. Next, the sintered body is processed by cutting, etc.
Products.

[0034]

(Example 1) Alloy steel powder (A, F) to be the first phase
~ I) and steel powder (e ~ g) to be the second phase are blended so as to have the composition ratio shown in Table 1. Further, C powder or, further, Cu powder to be the Cu phase, or Cr as hard particles. ,
An intermetallic compound composed of Mo and Co, or MnS or graphite as a solid lubricant is blended so as to have a ratio shown in Table 2, and 1% of zinc stearate is further blended as a lubricant and kneaded. The mold was filled, compressed and molded, and sintered at 1150 ° C. × 0.5 hr in an AX gas atmosphere.

The composition of the alloy steel powder used is as follows. A powder is 0.9 wt% C-4 wt% Cr-5 wt% Mo-6 wt%
W-2 wt% V-balance Fe (Test No.2-1, Test No.2-
2, used for Test No.2-10 and Test No.2-11). F powder is 1.2
wt% C-4wt% Cr-5wt% Mo-6wt% W-3wt% V-
The balance is Fe (Test No. 2-4, Test No. 2-5, Test No. 2-12
Used).

G powder is 1.5 wt% C-4 wt% Cr-12 wt% W
-5 wt% V-balance Fe (used in Test Nos. 2-6 and 2-7). H powder is 1.3 wt% C-4 wt% Cr-3 wt% Mo-10
wt% W-3wt% V-10wt% Co-balance Fe (Test No.2-
8)). I powder is 0.9 wt% C-4 wt% Cr-5 wt% Mo
-6 wt% W-2 wt% V-8 wt% Co-balance Fe (test N
o.2-9).

The composition of the steel powder used is as follows. e
The powder is 3 wt% Cr-balance Fe, and C is dissolved in the matrix at 0.8 wt% (Test No.2-1, Test No.2-2, Test No.2-3,
Test No.2-8, Test No.2-9, Test No.2-11, Test No.2-12
Used). The powder f is 1 wt% Cr-0.5 wt% Mo-balance Fe, and C is dissolved in the matrix at 0.8 wt% (Test No. 2-4,
Used for test No.2-5).

The g powder is 5 wt% Mo-balance Fe, and C is dissolved in the matrix at 0.8 wt% (Test No. 2-6, Test No. 2-7).
Used). The metal structures of these sintered bodies were observed, and an example of a metal structure photograph was shown in FIGS.
As shown in FIG. FIG. 1 is a photograph of a metal structure as polished, and FIG. 3 is a photograph of a metal structure that has been corroded by an etchant.

1 (a) and 3 (a) are photographs of an optical microscope structure of Test No. 2-1. FIGS. 1 (b) and 3 (b) are photographs of the test.
No.2-2 optical microscope structure photograph, Fig. 1 (c), Fig. 3 (c)
Fig. 2 is an optical micrograph of Test No. 2-3, and Fig. 2
FIG. 2A is a sketch drawing of the organization photograph of FIG.
(B) is a sketch drawing of the organization photograph of FIG. 1 (b), and FIG.
(C) is a sketch drawing of the organization photograph of FIG. 1 (c). FIG. 4A is a diagram of FIG. 3A, and FIG.
FIG. 4C is a sketch drawing of the structure photograph of FIG. 3C. In the sketch diagrams shown in FIGS. 2 and 4, H is the first phase, S is the second phase, C is the Cu phase, and V is the vacancy.

FIG. 5 is an optical micrograph of a comparative example (test No. 2-10). It has a structure in which vacancies and carbides are precipitated. The sintered bodies of the present invention and comparative examples were processed, processed into compressor vanes, and subjected to a wear test under the following test conditions using a high-pressure atmosphere wear tester shown in FIG. FIG. 7 shows the shape of the test piece used.

Test load: 150 kgf Circumferential speed: 500 rpm Test time: 3 hr Oil used: Ester oil Oil temperature: 110 ° C. Refrigerant used: R134a Atmospheric pressure: 13 kg / cm ³ Roller material: Monicro cast iron Table 1 shows the results.

[0042]

[Table 1]

From Table 1, it can be seen that the present invention within the scope of the present invention (test
In Nos. 2-1 to 2-9), the amount of wear of the vane is small, and the amount of wear of the roller is also small. Test No. 2-10, in which there was no second phase, and Test No. 2 in which the amount of Cu phase was outside the range of the present invention.
In the comparative examples of Test No. -11 and Test No. 2-12 in which the amount of the second phase was large, the wear amount of the vane and the roller was also large.

[0044]

According to the present invention, a sintered alloy material having excellent wear resistance can be obtained, and a sintered alloy material applicable to compressor parts such as a compressor vane and a scroll stopper ring under severe operating conditions can be obtained. It can be manufactured at low cost.

[Brief description of the drawings]

FIG. 1 is a photograph showing an optical microscopic structure of a sintered body of an example of the present invention in a state of being polished.

FIG. 2 is a sketch drawing of the optical microscope structure photograph shown in FIG.

FIG. 3 is a photograph showing an optical microscope structure of a sintered body of the present invention.

FIG. 4 is a sketch diagram of the optical microscope structure photograph shown in FIG.

FIGS. 5A and 5B are photographs showing an optical microscope structure of a sintered body of a comparative example, in which FIG. 5A is a photograph of a structure as polished, and FIG.

FIG. 6 is a schematic explanatory view of a high-pressure atmosphere wear tester.

FIG. 7 is an explanatory diagram showing dimensions and shapes of test pieces used for a high-pressure atmosphere wear test.

[Explanation of symbols]

 H First phase S Second phase C Cu phase D Hard particle L Solid lubricant A Base structure B Pearlite

──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. ⁶ Identification symbol FI F04C 29/00 F04C 29/00 U // C22C 33/02 103 C22C 33/02 103D

Claims (6)

[Claims] An iron-based base structure mainly composed of a mixed structure of a first phase containing Fe as a main component in which fine carbides are precipitated and a second phase containing Fe as a main component and softer than the first phase. Wherein the first phase is C: 2.
Including 0% or less, Cr: 17% or less, Mo: 12% or less, W: 20
%, V: 6% or less, Ti: 3% or less, Nb: 3% or less,
B: 1% or less selected from 3% or less and Co: 13% or less, the balance consisting of Fe and unavoidable impurities, and precipitation of fine carbides of 10 μm or less, hardening of 400 Hv or more The second phase has a composition of any of pure iron, carbon steel or low alloy steel, An iron-based sintered alloy material for compressor parts having excellent wear resistance, wherein the area ratio in the base structure is 5 to 70%. 2. The second phase is pure iron containing C: 0.5% or less, or C: 1.5% or less, Mn: 0.5% by weight.
% Or less, Si: carbon steel containing 1.0% or less, the balance being Fe and unavoidable impurities, or C: 1.5% or less, Mn:
0.5% or less, Si: 1.0% or less, Cr: 4% or less, M
o: 3% or less, Ni: 5% or less, V: 1.0% or less, Cu: 5.0
%. The compressor component according to claim 1, comprising one or more selected from low alloy steels containing at least one selected from the group consisting of Fe and unavoidable impurities. Iron-based sintered alloy material. 3. The method according to claim 1, wherein an infiltrated or pre-added Cu phase or Cu alloy phase is contained in an area ratio of 1 to 20% in addition to the iron-based matrix structure. Iron-based sintered alloy material for compressor parts. 4. An average particle size in addition to the iron-based matrix structure:
4. An iron-based sintered alloy for a compressor part according to claim 1, wherein hard particles having a hardness of 20 to 100 [mu] m and a hardness of 700 to 1500 Hv are dispersed in an area ratio of 1 to 20%. Wood. 5. The iron system for a compressor part according to claim 1, wherein a solid lubricant is contained in an area ratio of 0.5 to 10% in addition to the iron-based matrix structure. Sintered alloy material. 6. The iron-based sintered alloy material for a compressor part according to claim 1, wherein the sintered pores are infiltrated with a low melting point metal.