JP2002031045A - Swash plate compressor - Google Patents

Abstract

PROBLEM TO BE SOLVED: To improve the anti-seizure property between a swash plate and shoe of a swash plate compressor. SOLUTION: The spraying layer of the surface of swash plate is made of Al alloy, Cu alloy, or Au-Cu composite material, while the surface of the shoe is formed as a boron impregnation processed layer.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a swash plate compressor, and more particularly, to a swash plate compressor characterized by a new material combination of a shoe and a swash plate.

[0002]

2. Description of the Related Art A swash plate compressor includes a swash plate fixed to a rotating shaft at a fixed angle or a variable angle, a piston fitted in a cylinder provided parallel to the rotating shaft, and a swash plate and a piston. The piston is reciprocated by the rotation of the swash plate, and gas is introduced into the cylinder and compressed. The structure of the swash plate type compressor itself is, for example,
FIG. 1 and Publication No. 3, line 42 to column 4, line 16 of No. 1636,
See description at column 5, line 14 to column 6, line 2. As such a swash plate, quenched cast iron is used in the old days, and then Al-
Forged Si-based aluminum alloys are used, and at present, cast iron swash plates are used, especially from the viewpoint of the rotational performance of variable capacity compressors. A cast iron swash plate sprayed with an alloy is used. On the other hand, chrome steel,
In particular, bearing steel (SUJ2) is used.
No. 35190).

According to Japanese Patent Publication No. 4-77155, surface treatments such as nitriding, carbonitriding, carburizing, quenching, quenching and hardening, boron immersion, and nitrosulphurizing are listed as surface treatments for shoes. The swash plate as a mating material of the shoe in this publication is made of a hypereutectic Si aluminum alloy.

According to WO95 / 25224, Cu-Pb
It has been proposed to improve seizure resistance by unmelting a part of the lead structure when spraying an alloy. In this publication, as a mating shoe, "a ferrous material having a sliding surface made of any material containing iron as a main component can be used, but a bearing steel is preferable. There is no limitation at all, and techniques such as rolling, forging, powder metallurgy, and surface hardening can be appropriately adopted. " In the embodiment, a SUJ2 quenching shoe is used.

[0005]

When the boron-impregnated shoe is slid with a hypereutectic Si-aluminum alloy swash plate, abrasion resistance can be secured to some extent, but sufficient performance is obtained in terms of seizure resistance. Did not. On the other hand, when the sprayed swash plate of the Cu-Pb alloy was slid against the quenched bearing steel shoe, the seizure resistance was sufficient, but sufficient performance was not obtained in terms of the wear resistance of the shoe. An object of the present invention is to provide a swash plate compressor that can overcome these difficulties and can be used under more severe conditions than before.

[0006]

The inventors of the present invention have conducted experiments on various combinations of swash plate materials and shoe materials. It has been found that the seizure resistance and the wear resistance are superior to the combination. That is, the present invention relates to a swash plate compressor including a swash plate compressor, a piston, and a shoe sliding between the swash plate and the piston. -To provide a swash plate compressor characterized by combining the swash plate coated with an aluminum composite material and a shoe having a surface subjected to boron immersion treatment. Hereinafter, the present invention will be described in detail.

(1) Shoe The swash plate type compressor itself is a well-known shoe and is composed of a spherical portion fitted into a piston and a flat portion in contact with the swash plate. Saga 15
By using a convex curved surface having an extremely large radius of curvature of not more than μm and forming a chamfer on the outer peripheral edge of the flat portion, variations in seizure resistance are reduced (Japanese Patent Publication Nos. 61-1636 and 63-27554). Gazette, Japanese Patent Publication No. 1-35190). The shoe having such a convex portion and a chamfered portion is employed in an actual machine and greatly contributes to improving the performance of a swash plate of a swash plate type compressor. When the height of the convex portion is increased, an oil film is likely to be formed, but on the other hand, the variation in seizure resistance is increased. Therefore, a height range of 1 to 5 μm is adopted in a current actual machine. The boron immersion treatment of the shoe can be performed, for example, by the solid boron immersion treatment method described in US Pat. No. 5,082,512 according to the invention of Nimura et al. The structure of the boron-treated surface is defined in claims 1 to 5 of the patent.
5 may be used. In particular, a shoe containing Fe ₃ B in the surface structure or a shoe made of only Fe ₃ B can be preferably used for the shoe. The thickness of the boron-impregnated layer is preferably 5 to 100 μm, more preferably 10 to 30 μm.
μm. The surface roughness of the boron-impregnated layer is Rz 0.1
~ 1.0 µm is preferred. In addition, a salt bath method or the like can be used in addition to the solid method.

(2) Sprayed aluminum alloy Next, the aluminum alloy used for the sprayed surface layer of the swash plate is an aluminum alloy containing 12 to 60% by mass of Si, in which granular silicon is dispersed, and this alloy. A composite aluminum alloy in which carbon and / or MoS ₂ is dispersed in a matrix can be preferably used. here,
Carbon has a graphite structure, an amorphous carbon structure, or a degree of crystallization intermediate between the two. In the above-mentioned aluminum alloy, if the content of Si is less than 12% by mass, the wear resistance is not sufficient, and if the content exceeds 60% by mass, it becomes difficult to produce a raw material powder for thermal spraying. Silicon is finely and finely dispersed in an aluminum matrix in particulate form to enhance wear resistance. In the present invention, granular silicon refers to spherical, massive, polygonal, islands with irregular contours, which have almost the same dimension in any direction without a long directionality in one direction as seen in a rolled material or a cast material. It is an indefinite form not classified as. In addition, since the friction characteristics are insufficient with the aluminum alloy alone, the tribomaterial carbon and / or
Alternatively, MoS ₂ is dispersed.

[0009] As described above, the main component of the boron-impregnated layer is boride of iron, and has extremely excellent wear resistance. The sliding phenomenon between this substance and the above-mentioned substance constituting the thermal spray layer is considered as follows. (B) Aluminum matrix-iron boride: Relatively hard to adhere and hardly cause abrasion of both substances. (B) Granular silicon-iron boride: Both materials have very little wear. (C) Tribo material-iron boride: low coefficient of friction. Since such a phenomenon occurs in combination, it is considered that excellent sliding characteristics are realized by the combination of the present invention.

Next, in the present invention, Sn is added, and an Al-Si-Sn alloy having excellent wear resistance and seizure resistance can be used as an aluminum alloy. Sn
Is a component that is uniformly dispersed in aluminum to impart a lubricant and conformability. If the Sn content is less than 0.1% by mass, the effect of improving the lubricant and the like is small, and if it exceeds 30% by mass, the strength of the alloy is reduced. The preferred Sn content is 5
２５25% by mass. The Sn phase has a flake shape in the layer, and this shape is considered preferable in terms of lubricity.

The aluminum alloy of the present invention can contain, for example, the following optional elements. In addition, percentage is mass
%. Cu: Cu forms a solid solution in an aluminum matrix to increase the strength thereof, thereby suppressing the adhesive wear of aluminum and the wear due to the Si particles falling off. Further, Cu forms a part of Sn and an Sn-Cu intermetallic compound to enhance wear resistance. However, if the Cu content exceeds 8.0%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Cu content is 0.5 to 5
%. Mg: Mg combines with a part of Si to form an Mg-Si intermetallic compound and enhances wear resistance. However, when the content of Mg exceeds 3.0%, a coarse Mg phase is generated and the sliding characteristics deteriorate. Mn: Mn has a similar effect to Cu by forming a super-saturated solid solution in an aluminum matrix to increase its strength. However, when the content of Mn exceeds 3.0%, the alloy is excessively hardened and thus becomes unsuitable as a sliding member. The preferred Mn content is 0.1-1%. Fe: Fe is supersaturated in an aluminum matrix and has the same effect as Cu by increasing its strength. However, when the content of Fe exceeds 1.5%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Fe content is 0.1-1%. Ni: Ni has a similar effect to Cu by forming a solid solution in an aluminum matrix in a supersaturated manner to increase its strength. However, if the Ni content exceeds 8%, the alloy is excessively deteriorated, and thus becomes unsuitable as a sliding member. The preferred Ni content is 1.5% or less.

In the present invention, as a method for spraying aluminum alloy and tribomaterial, Tribodist Vol.
41, no. Various thermal spraying methods described on page 20, page 11 of FIG. 2 and FIG. 2 can be employed, and among them, high velocity gas flame thermal spraying (HVOF, high velocity oxifuel) can be preferably employed. Since this method has the characteristics described on page 20, right column, lines 4 to 13, the method is considered to provide a Si phase morphology having characteristics. Atomized powder such as Al-Si alloy and Al-Si-Sn alloy can be used as the thermal spray powder. These atomized powders may be completely melted on the substrate and then solidified, or a part of the atomized powder may be applied on the substrate in a molten state so that the structure of the powder remains. Thermal spraying conditions include
Oxygen pressure 0.9-1.2 MPa, fuel pressure 0.6-0.
9 MPa and a spray distance of 50 to 250 mm are preferred. The thickness of the sprayed layer is in the range from 10 to 500 μm, especially from 10 to 300 μm. The hardness of the aluminum alloy after thermal spraying is Hv1
It is in the range of 00 to 400. Since the hardness of a conventional 12% Si-containing aluminum alloy is Hv50 to 100, it can be said that the sprayed layer of the present invention is very hard.

Next, the phase dispersed in the aluminum alloy matrix by thermal spraying will be described. The material of the dispersed phase is sprayed together with the aluminum alloy or its raw material powder. According to the above-mentioned high-speed gas flame spraying method, these tribomaterials are relatively less likely to undergo combustion decomposition during thermal spraying and are taken into the sprayed layer. One dispersed phase is a carbonaceous material. As the carbon substance, amorphous carbon, graphite, carbon having a degree of crystallization intermediate between the two, and the like can be used. Graphite may be either natural graphite or artificial graphite. Regarding the tribological properties of these substances, graphite has strong cleavage properties, and this property can be used to enhance the sliding properties. When the carbonaceous material has a remarkable graphite structure, it exhibits the effect of cleavage, while as the two-dimensional structure becomes unclear, it exhibits abrasion resistance and enhances sliding characteristics. In addition, these carbonaceous materials are dispersed in the sprayed layer as they are in the sprayed layer so as not to melt during the spraying, while keeping the shape of the raw material powder relatively. MoS ₂ , another dispersed phase, is a well-known tribo material, but has little effect on improving the sliding properties of the sprayed layer under severe conditions, and improves the sliding properties under mild conditions, although not as much as graphite. Has the effect of doing The amount of the tribomaterial is preferably 2 to 40% by mass, more preferably 5 to 25% by mass, based on the sprayed layer. The average particle size of the tribomaterial before thermal spraying is preferably 10 to 50 μm, more preferably 20 to 40 μm.

In addition to the above-mentioned aluminum alloy and carbonaceous material and / or MoS ₂ , FeB, Fe ₃ P, Al
Hard materials such as ₂ O ₃ , SiO ₂ , SiC, and Si ₃ N ₄ can be added to improve wear resistance. These materials do not melt during thermal spraying but are dispersed in the alloy. The content of these hard materials is preferably 20% by weight or less based on the entire sprayed layer.

(3) Sprayed copper alloy In the present invention, a sprayable copper alloy for a sliding member, particularly C
A u-Pb alloy can be used. In this case, the sliding phenomenon between the thermal spray layer constituent material and the boride is considered as follows. (D) Copper matrix-iron boride: adhesion and wear of both materials are unlikely to occur. (E) Undissolved lead phase-iron boride: low wear coefficient. Since such a phenomenon occurs in combination, it is considered that excellent sliding characteristics are realized by the combination of the present invention.

As the copper alloy, those having the following composition (percentage is% by mass) and structure can be used. (A) less than or equal to 40% of lead, less than or equal to 30% of tin, less than or equal to 0.5% of phosphorus, less than or equal to 15% of aluminum,
10% or less silver, 5% or less silicon, 5% or less manganese, 5% or less chromium, 20% or less nickel and 30%
% Of at least one selected from the group consisting of zinc in an amount of 0.5 to 50%, with the balance being substantially copper and impurities. (B) A sprayed copper-based alloy containing 2 to 30% lead and substantially consisting of a mixed structure of an undissolved structure of a copper alloy atomized powder and a layered sprayed structure in which lead is forcibly dissolved in a copper alloy ( For example, Cu-Pb proposed in the above-mentioned WO95 / 25224 publication
alloy). (C) a sprayed layer made of a copper-based alloy containing 1 to 30% of lead has an undissolved structure of powder containing 3 to 40% of lead;
% Or less of a mixed structure with a dissolved structure containing or not containing less than 5% lead. (D) The sprayed copper alloy according to (c), wherein the lead phase in the undissolved structure is granular. (E) Al ₂ O ₃ , SiO ₂ , SiC, ZrO ₂ , Si
10% or less of one or more selected from the group consisting of ₃ N ₄ , BN, AlN, TiN, TiC, B ₄ C, and iron-based compounds of iron-phosphorus, iron-boron, iron-nitrogen An alloy further containing. (F) Further containing 3% or less of graphite (a) to (d)
Copper alloy.

(4) General Description of Sprayed Copper-Aluminum Composite Alloy In the present invention, a sprayed layer of a copper-aluminum composite material having excellent wear resistance and seizure resistance can be applied to a swash plate. The thermal spray layer is composed of a thermal sprayed copper-aluminum composite material including at least copper having a non-dissolved phase or a first copper alloy, and aluminum having at least a molten phase or a first aluminum alloy. In order to obtain a composite material of copper or copper alloy (collectively referred to as “copper alloy” in this paragraph) and aluminum or aluminum alloy (referred to as “aluminum alloy” in this paragraph), a part of these alloys must be melted. It is necessary to act as a binder. From another viewpoint, for example, Pb, Al in Cu-Pb alloy
It is necessary to avoid complete dissolution of the copper and aluminum alloys, since the Si in the -Si alloy interferes with the matrix properties of the other alloy and does not become a useful composite. In the present invention, if at least the aluminum alloy is dissolved, the binder effect for forming the composite material is realized. That is, copper and aluminum are originally compatible substances and are suitable for bonding.

General Description of Thermal Sprayed Structure An embodiment in which the composite material according to the present invention is composited with a copper alloy and an aluminum alloy will be described. This composite material can be obtained by a thermal spraying method. As a general tendency of thermal spraying, (a) when the average particle size of the copper alloy powder and the aluminum alloy powder are equal, the aluminum alloy powder dissolves, and (b) when the average particle size of the aluminum alloy powder is much larger than the copper alloy powder. Dissolves the latter in addition to the former. By utilizing such a tendency, it is possible to produce a copper-aluminum composite material in which at least a part of the aluminum alloy powder is dissolved and the remaining powder substantially maintains the solid property. Aluminum alloys have better wear resistance than copper alloys.Also, there are many aluminum alloys with excellent wear resistance in the cast state, so they are combined with copper alloys without being fully alloyed. By doing so, the wear resistance of the entire composite material can be improved as compared with the copper alloy. Considering these, the ratio of copper alloy and aluminum alloy is
It is preferable that the former is 80 to 30% by mass and the balance is the latter. In the present invention, the “dissolved phase” is a structure dissolved during thermal spraying of the copper-aluminum composite material. That is, according to most of the manufacturing processes, the metal material has been melted, but is in a state of being melted and solidified particularly during thermal spraying.

General theory of sprayed copper alloys and aluminum alloys
In the present invention, copper alloys and aluminum alloys include all alloys that can be sprayed. However, it is preferable to consider the following items. When the tempered state of a metal is roughly classified into a cast state and a processed state such as rolling and drawing, since a sprayed alloy belongs to the former cast state, cast copper alloys such as bronze, lead bronze, and phosphor bronze are preferred objects of the present invention. become.
On the other hand, since the copper-brought product used in the electronic equipment is an alloy in a processed and tempered state, it can be sprayed, but cannot exhibit its original performance. Similarly, wrought aluminum alloys are excluded from the present invention, and cast aluminum alloys such as Al-Si cast alloys having excellent wear resistance are preferred objects of the present invention. In addition, the first copper alloy and the first aluminum alloy also include a second copper alloy and a second aluminum alloy, respectively, in which the other component is partially mixed by thermal spraying and fused. That is, the composite material of the present invention excludes a state in which the copper alloy and the aluminum alloy are completely fused, but may partially fuse. Thus, the composite material of such an embodiment comprises a thermally sprayed copper alloy, a thermally sprayed aluminum alloy, and a thermally sprayed copper-aluminum alloy. In the following description, unless otherwise specified, the copper alloy and the aluminum alloy are alloys that do not include the second copper alloy and the second aluminum alloy, respectively.

Copper Alloy (One Component of Composite Material) In the present invention, the copper alloy is, by mass percentage, 40% or less of Pb, 30% or less of Sn, 0.5% or less of P, 15% or less of Al, 10% or less. % Or less of Ag, 5% or less of Mn, 5% or less of Cr, 20% or less of Ni, and 30% or less of Zn in a total amount of 0.5% or less.
%, Preferably 1% or more and 50% or less. Lead is the most preferred element for improving the sliding characteristics under dry conditions. However, if the lead content exceeds 40%, the strength of the copper alloy is reduced, so it is necessary to set the upper limit to 40%. The preferred lead content is 1
-30%, more preferably 2-15%. The additional elements other than lead mainly form a solid solution in copper to enhance its wear resistance and seizure resistance. Among them, Ag significantly enhances the sliding characteristics under the condition that the lubricating oil is small. Regarding the amount added,
Sn is precipitated at 10% or more and Mn is 1% or more, and the precipitate enhances wear resistance. Sn exceeds 30%, P is 0.5%
, Al exceeds 15%, Mn exceeds 5%, Cr
Is more than 5%, Ni is more than 20%, and Zn is more than 30%, the thermal conductivity inherent in copper, good sliding properties with iron or aluminum-based mating materials, especially abrasion resistance and seizure resistance Is lost. Therefore, it is necessary that these elements do not exceed the above upper limits. The preferred content is Sn:
0.1-20%, P: 0.2-0.5% or less, Ag:
0.1-8%, Mn: 0.5-4%, Cr: 0.5-3
%, Ni: 0.5 to 15%, Zn: 5 to 25%,
More preferably, Sn: 0.1 to 15%, Ag: 0.2
-5%, Mn: 0.5-3%, Cr: 1-2%, Ni:
1 to 10%, Zn: 10 to 20%. For the above reasons, the total amount of the added elements should be in the range of 0.5 to 50%. The first copper alloy containing these additional elements (however,
The second copper alloy (excluding the second copper alloy) is made of a Cu crystal in which these elements are dissolved (that is, a Cu solid solution) or a Cu crystal (including a Cu solid solution) and another phase. The other phases are a crystallization phase, a precipitation phase, a decomposition phase, and the like, and these phases are metals, intermetallic compounds, and other compounds such as Cu ₃ P. That is, if the first copper alloy (except for the second copper alloy) is made only of these compounds and the like, the original sliding characteristics of copper are not exhibited,
As described above, it is preferable that the Cu crystal be an essential component. However, the second copper alloy may be composed only of a compound or the like.

Aluminum alloy (a component of the composite material) In the present invention, the aluminum alloy is 12 to
Those containing 60% Si can be used.
If the Si content is less than 12%, the effect of improving the wear resistance and seizure resistance is small, and if it exceeds 60%, the strength is significantly reduced and the wear resistance is reduced. Preferred Si content is 15 to 50
%. If the size of the Si particles exceeds 50 μm, the Si particles will easily fall off. Preferred dimensions are 1 to 40μ
m. Next, the Al-Si-Sn based alloy is
It is a material that has excellent wear resistance and seizure resistance as wear and seizure resistant parts such as metals and bushes that used Sn alloys. Sn is a component that imparts lubricity and conformability, and is uniformly dispersed in the aluminum matrix. Sn adheres preferentially to the mating shaft, and prevents Al adhered to the mating shaft and Al of the bearing from sliding with each other by the same material, thereby improving seizure resistance. Sn content is 0.1
If it is less than 30%, the effect of improving lubricity or the like is small, and if it exceeds 30%, the strength of the alloy decreases. The preferred Sn content is 5 to 25%. Exists in the immediate vicinity of the Sn particle,
It is considered that fatigue resistance is improved by preventing coarsening of particles. Aluminum alloys can contain the following optional elements. Cu: Cu is supersaturated in the aluminum matrix to form a solid solution to increase the strength, thereby suppressing the adhesive wear of aluminum and the wear caused by the Si particles falling off. Further, Cu forms a part of Sn and an Sn-Cu intermetallic compound to enhance wear resistance. However, if the Cu content exceeds 7.0%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Cu content is 0.1.
5 to 5%. Mg: Mg combines with a part of Si to form an Mg-Si intermetallic compound and enhances wear resistance. However, if the Mg content exceeds 5.0%, a coarse Mg phase is generated, and the sliding characteristics deteriorate. Mn: Mn has a similar effect to Cu by forming a super-saturated solid solution in an aluminum matrix to increase its strength. However, when the content of Mn exceeds 1.5%, the alloy is excessively hardened and thus becomes unsuitable as a sliding member. The preferred Mn content is 0.1-1%. Fe: Fe is supersaturated in an aluminum matrix and has the same effect as Cu by increasing its strength. However, when the content of Fe exceeds 1.5%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Mn content is 0.1-1%. Cr: Cr has an effect of preventing coarsening of a soft phase such as Sn. However, if the content of Cr exceeds 5%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Cr content is 1-3%. Ni: Ni has a similar effect to Cu by forming a solid solution in an aluminum matrix in a supersaturated manner to increase its strength. However, if the Ni content exceeds 8%, the alloy is excessively hardened, and thus becomes unsuitable as a sliding member. The preferred Ni content is 0.1-5%. The first aluminum alloy containing these additional elements (excluding the second aluminum alloy) consists of an Al crystal in which these elements are dissolved (ie, an Al solid solution),
Alternatively, it is composed of an Al crystal (including an Al solid solution) and another phase. Other phases are crystallization phase, precipitation phase,
Decomposition phases and the like, these phases are metals, intermetallic compounds,
And other compounds. That is, if the first aluminum alloy (excluding the second aluminum alloy) is made only of these compounds, etc., the binder function of the aluminum alloy is not exerted, so that the Cu crystal is an essential component as described above. Is preferred. However, the second aluminum alloy may be composed only of a compound or the like.

Composition of the whole composite material (i) Combination of Cu-Pb-based alloy and Al-Si-based alloy A preferred combination of composite components in the present invention is a Pb-containing alloy in which a copper alloy has excellent seizure resistance, The aluminum alloy is a Si-containing alloy having excellent wear resistance. More specifically, a combination of a copper alloy containing 40% or less by weight of Pb and a 12 to 60% Si-Al alloy.
The overall composition of such a composite is, in mass percent, Cu:
8 to 82%, Al: 5 to 50%, Pb: 32% or less, S
i: 5 to 50% is preferable. (ii) Combination of Cu-Pb-based alloy and Al-Si-Sn-based alloy The overall composition of such a composite material is expressed by mass percentage of Cu:
8 to 82%, Al: 5 to 50%, Pb: 32% or less, S
Preferably, i is 5 to 50% and Sn is 21%. (iii) Combination of Cu-Pb-based alloy and Al-Si-X-based alloy In this combination, the aluminum alloy has an X component (Cu, M
g, Mn, Fe, Cr and / or Ni). The overall composition of this copper-aluminum composite material is, by mass percentage, Cu: 8 to 50%, Al: 15 to 50%, Pb:
32% or less, Si: 5 to 50%, Mn: 1.2% or less,
It is preferable that Cr: 5% or less, Ni: 4% or less, Mg: 4.0% or less, and Fe: 1.2% or less. When Sn is contained in addition to the X component, the content is preferably 24% or less. (iv) Combination of Cu-Pb-X-based alloy and Al-Si-based alloy In this combination, the copper alloy has an X component (Sn, P, Al, A
g, Mn, Cr, Ni and / or Zn). The composition of the entire composite material obtained by combining these is, in mass percentage,
Cu: 8 to 82%, Al: 5 to 50%, Pb: 32% or less, Si: 5 to 50%, Sn: 24% or less, P: 0.4
%, Ag: 8% or less, Mn: 4% or less, Cr: 4%
Hereinafter, it is preferable that Ni: 16% or less and Zn: 24% or less. (v) Combination of Cu-Pb-X-based alloy and Al-Si-Sn-based alloy The composition of the entire composite material obtained by combining them is, in terms of mass percentage, Cu: 8 to 50%, Al: 15 to 50%, Pb: 3
2% or less, Si: 5 to 50%, Sn: 30% or less, P:
0.4% or less, Ag: 8% or less, Mn: 4% or less, C
It is preferable that r: 4% or less, Ni: 16% or less, and Zn: 24% or less. (vi) Combination of Cu-Pb-X-based alloy and Al-Si-X-based alloy The composition of the entire composite material obtained by combining them is, in terms of mass percentage, Cu: 8 to 50%, Al: 15 to 50%, Pb: 3
0% or less, Si: 5 to 50%, Sn: 24% or less, P:
0.4% or less, Ag: 8% or less, Mn: 5% or less, C
r: 8% or less, Ni: 20% or less, Zn: 24% or less,
It is preferable that Mg: 4.0% or less and Fe: 1% or less (claim 21). When Sn is contained in addition to the X component, the content is preferably 30% or less.

(F) Sprayed metallographic structure Before describing the structural characteristics of the copper-aluminum composite material of the present invention, general features of the metallographic structure of the sprayed layer will be described.
This is a structure obtained by melting and solidifying a powder such as an atomized powder. In one form, the droplets generated by melting in the thermal spray frame are deformed by colliding with the substrate surface, and when viewed in layer cross section,
The laminar, flaky, or flat plate-like portions have small disks, scale-like pieces, etc. stacked in the plane of the layer. In yet another form, when the powder such as atomized powder is pumped into the frame by gas, it retains the form of isolated particles in which each is dispersed, and a part of the particles is united, but in the form as it is. It is thought to melt. The molten droplet collides with the base material and solidifies, but if the thickness of the sprayed layer is reduced and the cooling is accelerated, one or several droplets do not coalesce with many other droplets due to fusion etc. Solidifies as independent particles. In this way, relatively small droplets are crushed, and a large number of fine layered pieces are stacked as a whole to form a sprayed layer. In other forms, the droplets coalesce into a large layer and solidify.

(G) Thermal spray composite structure In the present invention, the copper alloy powder is contained in the thermal spray layer without being dissolved at least during thermal spraying, and the mixed structure of the molten phase of the aluminum alloy and the undissolved phase of the copper alloy powder is formed. Is formed. The undissolved phase of the copper alloy powder constituting this structure is a structure in which the structure of the copper alloy powder does not disappear even during the spraying flame and remains in the sprayed layer. Therefore, the dissolved phase is a normal spray-dissolved tissue having the form described in the preceding paragraph (f), that is, a tissue dissolved during thermal spraying, and an undissolved phase is a tissue that does not dissolve during thermal spraying. The undissolved phase lacks some of the morphologies as described in (f) above, as exemplified below. Alternatively, the undissolved phase can be distinguished from the dissolved phase by an optical microscope in the following points.

The dissolved phase coalesces and melts, the undissolved phase does not coalesce. The dissolved phase has a large deformation due to collision, and the undissolved phase has a small deformation due to collision. In the case of an alloy such as Cu-Pb, P constituting the secondary phase
Focusing on b, the dissolved phase and the undissolved phase can sometimes be distinguished. Since the Al alloy phase of the thermal sprayed layer is composed of a pattern having a similar form, it may be difficult to determine the above by (1). In this case, it is impossible to determine the crystal grain boundary, and when it looks like a continuous phase at a glance and the secondary phase also has a uniform morphology, it can be determined to be a dissolved structure. When the Al alloy phase of the thermal spray layer is composed of particles of the same form, it is compared with known powder forms such as atomized powder, pulverized powder, and electrolytic powder. A part of copper alloy powder and aluminum alloy powder fuse,
Thereafter, the Cu-based secondary phase is dispersed from the aluminum matrix.
This is the molten phase of the second aluminum alloy referred to in the present invention. Note that this secondary phase is easily distinguished from other tissues. When a part of the copper alloy powder is melted, the aluminum alloy is taken in, and then the Al-based secondary phase is precipitated and dispersed from the copper matrix, such a structure is a dissolved phase of the second copper alloy. Also, when the taken-in aluminum remains in a solid solution state, it is also a dissolved phase of the second copper alloy. Since the copper alloy always has an undissolved structure, it is easy to distinguish the dissolved structure of the copper alloy from the undissolved structure.

In the present invention, the ratio of the copper alloy to the aluminum alloy is preferably 80 to 30% by mass and the balance is the latter by mass. The main structure of the copper-aluminum composite material of the present invention is at least two types of (a) copper alloy dissolved structure, (b) copper alloy undissolved structure, (c) aluminum alloy dissolved structure, and (ii) aluminum alloy undissolved structure. (However, only (A), (C) only and (B), (D)
Only combinations). In the present invention, a part of the powder does not dissolve during the thermal spraying and remains in the thermal sprayed layer to form a mixed structure of a dissolved structure and an undissolved structure of the powder.
This feature is first described for Cu-Pb alloys,
The -Si alloy will be described later. The undissolved structure of the lead bronze powder constituting this structure is such that the rapidly quenched structure of the lead bronze powder does not disappear during the spraying flame and remains in the sprayed layer. In this structure, a phase containing lead as a main component is dispersed in fine particles or is distributed in layers at copper grain boundaries. This structure is a kind of casting structure, but it is characterized by (a) the main cooling direction is the direction from the periphery of the particles to the inside, and (b) a quenching structure rather than ordinary ingot casting or continuous casting. There is.

In the present invention, when the copper alloy and the aluminum alloy are completely fused, for example, Si in the Al alloy becomes Cu
In order to produce a coarse intermetallic compound when a melt is formed and solidified to produce a Cu-Al-Pb-Si alloy having no practical use, a combination consisting only of the above structures (a) and (c) Is excluded. In other words, under the condition that the copper alloy melting structure (a) and the aluminum alloy melting structure (c) are generated, the molten copper alloy and the molten aluminum alloy are almost completely fused unless the undissolved powder coexists. It is necessary to avoid a thermal spraying method in which only (c) exists. The presence of (b) and / or (d) in the structures (a) and (c) prevents fusion of the copper / aluminum alloy. Furthermore, at the interface between the undissolved structure of the copper alloy of (a) and the undissolved structure of the aluminum alloy of (d), and the interface between the dissolved structure of the aluminum alloy (c) and the structure of the undissolved copper alloy (b), both alloys have low melting points Fusion occurs with the formation of material, but to a lesser extent. Therefore, in the present invention, such an interface structure is not included in the main structure, and the main structure is separated into (a), (b), (c), and (d) in the structure state of the molten powder. From the above, the combination of the structures of the copper-aluminum composite material in the present invention is as follows:

A. (A) + (ii) B. (A) + (b) + (ii) C.I. (B) + (c) D. (B) + (c) + (ii) (A) + (b) + (c) (A) + (b) + (c) + (ii) (A) + (c) + (ii). Composite material having unmelted Cu alloy structure (B, C, D, E,
In F), the fine Pb phase in the atomized powder remains in the sprayed layer and contributes to the improvement of sliding characteristics. Dissolved Cu-Pb alloy powders (A, B, E, F, G) have a large Pb phase when Cu and Pb are melted and solidified. A composite material having a Si alloy structure is bonded. At this time, the surface of the powder is often melted (F, G). The composite material (C, D, E, F, G) having a molten Al alloy structure is formed in a sprayed layer in one direction, such as the primary crystal Si of a conventional molten alloy or the Si particles of a rolled alloy. It is not a particle shape having a clearly long direction, but granular Si particles having a spherical shape, a massive shape, a polygonal shape, and other irregular shapes that are not classified into these are dispersed in almost any direction. Further, in the case of the present invention, it is difficult to distinguish between the primary crystal Si and the eutectic Si which are obvious in the conventional ingot alloy. Also, by the reaction occurring between the molten Al-Si alloy powder and the Cu-Pb alloy powder,
The latter powder is combined.

(H) Characteristics of Composite Material The characteristics of each of the constituent alloy phases of the copper-aluminum composite material having these structures will be described with respect to examples of Cu-Pb alloy and Al-Si alloy. (A) In the undissolved copper alloy, the fine Pb phase in the copper alloy powder such as atomized remains in the sprayed layer and contributes to the improvement of the sliding characteristics. Furthermore, when the components of the aluminum alloy (dissolved or not dissolved), that is, Al, Si, etc., are dissolved in the copper alloy, the properties of copper that are difficult to adhere to may be weakened, but the undissolved copper alloy may prevent this. it can. (B) In the molten Cu-Pb alloy, when Cu and Pb are melted and solidified, the Pb phase becomes coarse, and molten Cu, Pb and Al-S
The reaction between the i-alloy powders binds the Al-Si alloy powder. At this time, the surface of the powder is often melted. (C) The molten Al alloy does not have a particle shape that has a clearly long one-way direction in the thermal sprayed layer, as found in the primary crystal Si of the conventional molten alloy and the Si particles of the rolled alloy. In any direction, granular Si having almost the same size, spherical, massive, polygonal, and other irregular shapes that are not classified into these are dispersed. Further, in the case of the present invention, it is difficult to distinguish between primary crystal eutectic Si and eutectic Si, which is obvious in the conventional ingot alloy. The improvement in wear resistance is large due to such a Si structure. The reaction between the molten Al-Si alloy powder and the solid Cu-Pb alloy powder combines the latter powder. In general, the hardness of a material obtained by combining a hard material and a soft material is in the middle of these values. However, in the composite material of the present invention, a reaction phase of a copper alloy and an aluminum alloy may be formed. The average value of becomes higher.

(I) Thermal Spraying Method Next, a method of forming a composite sliding layer by thermal spraying will be specifically described. In the present invention, the second of the above tribologists
Various thermal spraying methods described on page 0 and FIG. 2 can be employed. Among them, high-speed gas flame spraying (HVOF, High v
elocity oxyfuel) can be preferably employed.
This method has been described in the 4-13 line right column page the first 20 "... high velocity gas flame spraying method (HVOF, H igh V elocity O x
y in f uel), the method combustion takes place in cancer interior (combustion chamber), oxygen (0.4～0.6MPa), fuel gas (0.
The pressure of the gas jet is very high, and the particle velocity is comparable to explosive spraying. Various thermal spraying methods have been developed that fall into the HVOF family, including diamond jets, top guns, and continuous explosive systems. Therefore, it is considered that Si and Sn particle morphologies having characteristics can be obtained. Since the sprayed Al is hardened by rapid solidification,
As a sprayed powder that has a feature of high i-particle holding power and can suppress abrasion due to Si particles falling off,
Atomized powder such as u-Pb alloy, Al-Si alloy, Al-Si-Sn alloy can be used. The spraying conditions were: oxygen pressure 0.45 to 0.76 MPa, fuel pressure 0.45 to 0.76 MPa, spraying distance 50 to 250
mm is preferred. The thickness of the sprayed layer is preferably from 10 to 500 μm. Subsequently, an average powder particle size adjusting method will be described as a method for producing the above-described various composite materials A to G. Table 1 shows an example of mixing an aluminum alloy powder similar to a copper alloy powder having a particle size showing a normal distribution around one average value, and further, coarse particles having one or both of a copper alloy and an aluminum alloy having a normal distribution particle size. Table 2 shows an example of mixing fine particles.

[0031]

FIG.

[0032]

FIG. 2 When the combination of fine powder Cu-Pb and coarse powder Al-Si in Table 2 is selected, the amount of copper alloy dissolved can be increased.

Embodiments of Other Composite Materials Various metal substrates such as iron, copper, and aluminum can be used as the substrate on which the sprayed layer is formed. The shape of the substrate is arbitrary, such as a plate, a disk, and a tube. The surface of the substrate is preferably Rz10 by shot blasting or the like.
If the surface is roughened to a surface roughness of 60 μm, the adhesion strength of the film increases. The hardness can be adjusted by subjecting the sprayed layer to heat treatment. At this time, some tissues may be dissolved.

The above-mentioned copper-aluminum composite material, in terms of mass percentage, is 30% or less, preferably 10% or less, more preferably 1 to 10% of Al ₂ O ₃ , SiO ₂ , SiC, Z
rO ₂ , Si ₃ N ₄ , BN, AlN, TiN, TiC, B ₄
C, and selected from the group consisting of iron-phosphorus compounds, iron-phosphorus compounds, iron-boron compounds, iron-nitrogen compounds
One or more compounds can be added as a wear resistance improving component. If the added amount of these components exceeds 30%, lubricity and conformability become poor, and as a result, seizure tends to occur.

Furthermore, in the present invention, the entire composite material can contain 30% or less by mass of graphite. Graphite is an additive that improves lubricity and prevents cracking of the sliding layer. If the graphite content exceeds 30%, the strength of the sprayed layer is undesirably reduced. The preferred graphite content is 1.5 to 15%.

Further, in the present invention, bronze containing 3% by mass or less of graphite in mass percentage can be sprayed. Graphite is an additive that improves lubricity and prevents cracking of the swash plate sliding layer. If the graphite content exceeds 3%, the strength of the bronze decreases, which is not preferable. The preferred graphite content is 0.15 to 1.5%. Above (a) ~
The description of (i)-except for the additional elements such as Si and Pb-also applies to pure copper-pure aluminum composite materials that are not alloys.

(5) Substrate As the substrate on which the thermal sprayed layer is formed, various metal substrates such as iron, copper, and aluminum can be used. The surface of the substrate is preferably shot at Rz10 by shot blasting or the like.
When the surface is roughened to a surface roughness of ６０60 μm, the adhesion strength of the film increases. Specifically, the adhesion strength of the sprayed Ni film to the steel substrate (shot blast) is 30 to 50 MPa, while the adhesion strength of the coating of the present invention is 30 to 60 MPa. .
Therefore, according to the present invention, the same adhesive strength as that of the Ni sprayed coating which is conventionally considered to have good adhesiveness can be obtained.

In the present invention, copper, nickel, aluminum, a copper-nickel alloy, a nickel aluminum alloy, a copper aluminum alloy, a copper tin System alloy, nickel self-fluxing alloy and cobalt self-fluxing alloy, an intermediate layer made of one or more materials selected from the group consisting of plating, sputtering,
It is preferably formed by a method such as thermal spraying. All of these materials require their surfaces to be rough, but since they are easily alloyed with bronze, they are firmly bonded to the (un) dissolved layer during thermal spraying and are bonded to the thermal spray layer and back metal. Increase strength. The preferred thickness of the intermediate layer is 5 to 100 μm. As the copper-tin alloy, a Cu-Sn-P-based alloy can be used. Since this alloy has a good molten metal flow and is hard to be oxidized, excellent performance can be obtained when the intermediate layer is formed by thermal spraying. The hardness can be adjusted by subjecting the sprayed layer to heat treatment.

(6) Overlay In the case where the sprayed layer is used without an overlay, the surface of the sprayed layer is preferably finished to Rz 3.2 μm or less. When an overlay is used, a soft metal such as Sn-based or Pb-Sn, or a solid lubricant such as MoS ₂ , graphite, or MoS ₂ + graphite can be used. The combination of the above-mentioned soft coating and the sprayed layer dramatically improves seizure resistance, and provides performance exceeding that of bronze-based sliding materials. As described above, MoS ₂ present in the sprayed layer has little effect of improving the sliding characteristics under severe conditions such that there is no refrigerating machine oil, but MoS ₂ as an overlay exhibits an outstanding effect.

[0040]

Example 1 A shoe was boron-impregnated by the following method. That is, boron carbide B ₄ a shoe material made of SUJ2 material diameter 13mm
C, the material is buried in a powdered material obtained by adding silicon carbide and potassium boron tetrafluoride KBF ₄ to carbon, and 800 to 1000
Heated to 3 ° C for 3-5 hours. By this treatment, a boron-impregnated layer made of FeB on the outside and Fe ₂ B on the inside was formed to a thickness of about 50 μm. The hardness of this layer was Hv1300. 40% Si-Al
An alloy (A2024) having an average particle size of 75 μm was prepared.
On the other hand, a commercially pure rolled aluminum plate was subjected to shot blasting using a steel grid (size 0.7 mm), and the surface was roughened to a roughness Rz of 45 μm to obtain a swash plate material. HV
Using an OF type thermal spraying machine (DJ manufactured by Sulzer Metco), thermal spraying was performed under the following conditions. Oxygen pressure: 1.0 Mpa Fuel pressure: 0.7 Mpa Spray distance: 180 mm Thickness of sprayed layer: 200 μm As a result of this spraying, hardness Hv _0.3 = 210, average granular Si
The particle size was 5 μm.

The seizure resistance test was performed using the tester shown in FIG. 1 under the following conditions. (1) Sliding speed: 15 m / sec (1790 rpm) (2) Load: 390 N / 10 mm (gradual increase in load) (3) Lubrication: refrigeration oil 1: light oil 9 (4) Lubrication method: drip method: 25 drops / mm In 1, 1 a and 1 b are shoes, 2 is a swash plate equivalent material,
3 is a lubricating oil. The test results are shown in FIG. 2 together with the other examples.

Example 2 In place of the 40% Si-Al alloy used in Example 1, 36% Si was used.
Using an -Al alloy, 90% by mass of this aluminum alloy and graphite (average particle size: 30 m) were sprayed. FIG. 2 shows the results of a test performed in the same manner as in Example 1.

Comparative Example 1 In place of the thermal spray swash plate used in Example 1, a hypereutectic Al-Si alloy not subjected to thermal spraying was used as a swash plate equivalent material. The results are shown in FIG.

Example 3 In place of the aluminum alloy powder used in Example 1, Cu
Using -10% Sn-10% Pb atomized powder (average particle size 50 μm), thermal spraying was performed under the following conditions. Oxygen pressure: 0.6 MPa Fuel pressure: 0.6 MPa Spraying distance: 180 mm Thickness of sprayed layer: 300 μm In addition to the seizure resistance test described above, a wear resistance test was performed by pressing the shoe against a disc-shaped swash plate equivalent material. . The test conditions were as follows. (1) Sliding speed: 2.6 m / s (310 rpm) (2) Surface pressure: 4 MPa (3) Lubricating oil: refrigerating machine oil: refrigerant = 1: 9 (4) Time: 20 hrs FIG. FIG. 3 shows the results of the wear resistance test.

Comparative Example 2 A test was performed in the same manner as in Example 3 except that a shoe (hardness Hv780) without boron immersion was used instead of the shoe used in Example 3, that is, the SUJ2 shoe subjected to boron immersion in Example 1. The results are shown in FIGS.

Although the aluminum alloy swash plate has poor seizure resistance, the sprayed swash plate has very good seizure resistance. Further, the combination of the copper alloy swash plate and the bearing steel shoe causes the shoe to be easily worn, but the wear resistance can be improved by the boron immersion treatment of the shoe.

[0047]

As described above, according to the present invention, a combination of a swash plate and a shoe having better seizure resistance than before can be obtained, so that the swash plate type compressor can be adapted to severe operating conditions.

[Brief description of the drawings]

FIG. 1 is an explanatory diagram of a seizure test method.

FIG. 2 is a graph showing the results of a seizure test.

FIG. 3 is a graph showing a wear test result.

[Explanation of symbols]

 1-Shoe 2-Swash plate equivalent material 3-Lubricant

──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. ⁷ Identification symbol FI Theme coat ゛ (Reference) F04B 27/08 HL (72) Inventor Shibata Itojiro 3-65 Midorigaoka, Toyota-shi, Aichi Pref. In-house F term (reference) 3H076 AA05 BB26 CC20 CC33 4K031 AA02 AB02 BA05 CB09 CB12 CB15 CB35 CB37 DA01

Claims (2)

[Claims] 1. A swash plate compressor comprising a swash plate compressor, a piston, and a shoe sliding between the swash plate and the piston. A swash plate compressor comprising a combination of the swash plate coated with a copper-aluminum alloy composite material and a shoe whose surface is subjected to boron immersion treatment. 2. The boron-impregnated surface of the shoe is Fe ₃ B
The swash plate compressor according to claim 1, comprising: