JP3388476B2 - Aluminum-based composite sliding material and method for producing the same - Google Patents

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a sliding material and a manufacturing method thereof, and more specifically,
Pb, In, Cd, Sn, MoS ₂ , graphite, B
The present invention relates to an aluminum-based composite sliding material in which a lubricant such as N is compounded with aluminum or an aluminum alloy (hereinafter referred to as "aluminum") and a manufacturing method.

Further, the present invention relates to an aluminum-based composite sliding material in which a hard material made of so-called ceramic such as oxide, nitride or boride is compounded with aluminum in addition to such a lubricant, and a method for producing the same. .
The above-mentioned sliding material can be suitably used for sliding parts such as sliding bearings and bushes and washers of various devices such as internal combustion engines and compressors.

[0003]

2. Description of the Related Art The production of the above sliding material by sintering is disclosed, for example, in Japanese Patent Publication No. 61-17895 and Japanese Patent Publication No.
It is generally performed as described in Japanese Patent No. 27122. Further, Japanese Examined Patent Publication No. 3-22458 describes a method of mixing powders that have been composited by mechanical alloying with a Henschel mixer and hot extruding in a container.

It is also known to increase the density by rolling the sintered sliding material together with a supporting substrate, or to increase the density of the powder by rolling the powder together with the supporting substrate before sintering. .

Further, Japanese Patent Application Laid-Open No. Sho 5 (1994) filed by one of the present inventors
In JP-A-153706, a mixture of matrix alloy particles laminated on a substrate and reinforcing particles such as alumina is pressed in a semi-molten state in which the solid phase of the former is 50% or more as a method for producing a particle dispersion strengthened laminated material. , A method of pressure molding with a roll or the like is described. According to this description, the structure of the laminated layer after processing is composed of alloy particles that remain in the solid phase during processing, alloy phases that flow around them and solidify, and strengthening particles.

[0006]

In the conventional aluminum-based sliding material by sintering, the oxide film on the surface of aluminum particles significantly impairs the sinterability, so that the sintering between the composite additive and aluminum also becomes defective. . Further, liquid phase sintering has been performed to raise the sintering temperature to a temperature at which a part of aluminum becomes liquid phase. However, liquid phase sintering is performed by destroying the oxide film on the surface of aluminum particles. In order to bring out the effect of, the sintering temperature must be extremely high. Further, since the particles of the composite additive remain in the final sintered body in a dispersed state during the preparation of the raw material powder, there is a limit to fine and uniform dispersion, and further the composite additive moves in the aluminum liquid phase. Then, the fine and uniform dispersion state is impaired by approaching or coalescing.

[0007] Further, when an expansion process such as rolling is performed in the process of compounding or in the post-process, the soft additives such as Pb and graphite are stretched in the rolling direction to lower the material strength, and the bending process of the product and During cutting, the sliding layer cracks or peels off from the supporting substrate.

[0008]

In the aluminum-based composite sliding material according to the present invention, the sliding layer deposited on the supporting base material has the expandable lubricant particles in the aluminum alloy phase in a volume ratio of 1 to 1. 30% dispersed, aluminum alloy phase,
It is characterized by comprising a secondary phase fluidized and solidified under compression and a recrystallized matrix phase. In the above sliding material, hard material particles may be further dispersed in the sliding layer in an amount of 0.5 to 10% by volume.

Further, in the method for producing an aluminum-based composite sliding material according to the present invention, a mixture containing an aluminum alloy powder forming a layer on a supporting base material and a lubricant powder is added to the aluminum alloy powder. While substantially all maintaining the particle morphology, the particles are heated to a temperature at which the inside of the particles melts, and thereafter, the supporting base material and the mixture are subjected to a process of cooling while applying a compressive force.

Further, in another production method of the present invention, a mixture containing aluminum or aluminum alloy powder and extendable lubricant powder is molded into a plate-like material in which particle morphology remains to prepare a supporting substrate. Then, the plate-shaped material together with the supporting base material is heated to a temperature at which substantially all of the aluminum or aluminum alloy powder maintains the particle morphology and the inside of the particles melts, and then the supporting base material and the plate-shaped material. It is characterized in that it is subjected to processing to apply compressive force to and cooled.

In the above manufacturing method, the supporting base material is an aluminum-based material, and the supporting base material and the mixture are subjected to a process of cooling while applying a compressive force to form an aluminum-based composite material. You may press-contact a non-aluminum type material. Alternatively, in still another manufacturing method of the present invention, the plate-shaped material heated to a predetermined temperature may be subjected to a process of cooling while applying a compressive force, and then may be pressed into contact with the supporting base material.

In these manufacturing methods, hard particles may be mixed with the mixture containing aluminum alloy powder and lubricant powder. Hereinafter, the constitution of the present invention will be described in detail. In the present invention, the lubricant is intended to be blended as extendable particles, and graphite,
So-called solid lubricants such as MoS ₂ and soft BN, or soft metals or alloys such as Pb, In, Cd, and Sn. If the proportion of the lubricant is less than 1% by volume, the effect will be insufficient, while if it exceeds 30% by volume, the strength of the sliding material will be insufficient and delamination will be likely to occur. It is preferable that the size of the lubricant (the particle size of the particles, for needle-like ones, a value obtained by averaging a value such as 0.5 times the total value of the length and the width for all the particles) is 0.5 to 50 μm. .

As the aluminum, industrial pure aluminum or aluminum alloy can be used. In the case of aluminum alloys, alloy elements having a solid-liquid coexisting composition can be blended. From this viewpoint, preferably 1 to 10% Cu or 3 to 8
% Si can be blended. As an aging precipitation element, 5% or less of Cu, Mg, etc. can be contained. As the soft phase forming element, 30% or less of Sn, Pb, In or the like can be contained.
3% or less of Mn, Mo, or Cr can be used as an element which forms a hardened phase by forming an intermetallic compound and precipitating alone. The average particle size of aluminum powder is 5 to 100
It is preferably μm.

In the present invention, the hard material is so-called ceramic particles such as oxides, carbides, nitrides and borides, whiskers or short fibers. If the proportion of hard particles is less than 0.5% by volume, the wear resistance and seizure resistance of the sliding material will be insufficient, while if it exceeds 10% by weight, the stretchability of the lubricant will be affected and the interphase Due to insufficient adhesive strength, the sliding material also lacks abrasion resistance, seizure resistance, and fatigue resistance.

The size of the hard material (the particle diameter of the particles, for needle-shaped materials, the average value of 0.5 times the sum of the length and the width of all the material particles) is 0.5 to 10 μm. It is preferable. If the size of the hard material is less than 0.5 μm, the hard material particles easily aggregate to form a lump, and it becomes difficult for the liquid phase of aluminum to be described later to enter into the lump, and the adhesion force of the particles is insufficient, The sliding material has insufficient wear resistance and seizure resistance. On the other hand, when the size of the hard material exceeds 10 μm, the mating material is easily worn by the hard material.

The supporting base material is an aluminum-based material,
Industrial pure aluminum and aluminum alloy can be used. As the aluminum alloy, an aluminum bearing alloy, an wrought aluminum alloy, or the like can be used. As the non-aluminum material, a steel plate, an antioxidant surface-treated steel plate, a plated steel plate, a clad steel plate, a copper alloy plate, or the like can be used. Alternatively, a composite base material such as a bimetal material obtained by further adhering these to a steel plate or the like can also be used. It is also possible to use a metal container and fill it with the mixed powder.

Next, the structure of the composite sliding material according to the present invention will be described. The aluminum phase of the present invention comprises a secondary phase fluidized and solidified under compression and a recrystallized matrix phase. The latter is the main phase of the composite sliding material, and exhibits the properties as an aluminum sliding material and retains the composite components such as lubricant and hard material. The former enhances the binding force between each component.

In the case of the conventional liquid phase sintered phase, a liquid phase is generated by being heated above the solidus line of the aluminum raw material, and the liquid phase melts the oxide film on the surface of the aluminum powder to thereby improve the sinterability. The liquid phase is generated by heating the surface of each particle and further increasing the adhesive strength of each component of the sintered material, but the liquid phase is simply solidified and does not flow under compression. The matrix phase is not plastically deformed. Furthermore, in the conventional wrought processing method, the matrix phase plastically deforms,
No liquid phase has occurred. The features of these conventional tissues are shown in FIGS. 2 and 3, respectively, and the features of the present invention are shown in FIG.
Shown in.

FIG. 2 shows a liquid phase sintered structure, in which the composite material powder remains in the dispersed state (see FIG. 4) when it is a green compact, and the aggregated state is maintained as it is. Most of the grains maintain their original form. Although the sintered material may be subjected to post-processing such as sizing to improve the density, the above characteristics are maintained. FIG. 3 shows the wrought processed structure, in which the soft additive is markedly wrought.

On the other hand, in the structure of the present invention (FIG. 1), the matrix phase of aluminum has a grain boundary different from the crystal grain boundary resulting from the raw material powder by recrystallization. This is due to the generation of new grain boundaries due to plastic deformation under the compressive stress above the recrystallization temperature. Further, the crystal grains of the matrix phase have a directionality in the direction perpendicular to the direction of compressive stress. Further, the liquid phase not only improves the sinterability as in the conventional liquid phase sintering, but also causes the flow of the additive when flowing under the compressive stress, and the liquid phase is formed between the masses of the additive. Because of the inclusion of the, the additive is more finely and uniformly dispersed than the dispersed state at the time of the raw material.

The liquid phase may be generated from the above-mentioned matrix phase aluminum powder, or an aluminum powder whose composition is adjusted so that the liquid phase is easily generated is used separately from the matrix aluminum powder, It may be generated from now on. However, the former is more preferable.

Plastic working may be carried out to improve the density, dimensional accuracy and the like of usually 1 to 25% or less, preferably 5 to 20% without impairing the characteristics of the structure described above. In this case, when the degree of plastic working increases, the secondary phase becomes a plastic working structure that extends in the working direction.

Incidentally, the preferable plastic working (reduction ratio per rolling) in the semi-melt rolling is 25 to 60%. More preferable plastic working in the semi-melt rolling (reduction ratio per rolling) is 25 to 35 when it is desired to further suppress the elongation of the structure.
%, And if productivity is more emphasized, it may be 40 to 50%. Needless to say, the plastic working may exceed 60% in total when the process including the semi-melt rolling is performed plural times.

The form of dispersion of the extensible lubricant differs depending on the high melting point substance such as MoS ₂ and the low melting point substance such as Pb. Refractory material: a mass of the material is shredded by the forcedly flowing aluminum liquid phase in liquid phase sintering significantly more effectively than shredding by the liquid phase flowing simply by surface tension, and The particles are much smaller and slightly stretched in the processing direction than in conventional spreading methods.

Low-melting substance: Pb, for example, Pb flows due to surface tension before or after processing force is applied. When a processing force is applied, the aluminum liquid phase flowing out from the aluminum particles and a part of the Pb liquid are fused and fluidized and solidified together. The remaining part which is not fused is fluidized and solidified as a Pb phase. Such a Pb structure remarkably enhances seizure resistance and wear resistance (see the invention product 6 in Table 2 and comparison D).

Coexistence of high-melting-point substance and low-melting-point substance: The above-mentioned structure appears at the same time. Also, due to the Pb liquid phase, MoS
A lump of refractory material such as ₂ is shredded. As a result, seizure resistance and wear resistance are further enhanced (the product of the present invention 8 in Table 2).
reference). Next, a preferable manufacturing method of the present invention will be described.

First, a mixture containing aluminum or aluminum alloy powder (hereinafter referred to as "aluminum powder"), lubricant powder and hard material powder is laminated on a supporting base material. At this time, if necessary, the mixed powder may be compressed to increase the density so that the supporting base material and the powder mixture can be treated as one solid body by appearance, and each component is finely distributed by mechanical alloying. Good. The thickness of the layer is not particularly limited, but is generally in the range of 100 μm to 10 mm. Subsequently, heating is performed to a temperature at which substantially all of the aluminum maintains the particle morphology and the inside of the particles melts. Here, the density of the layer corresponds to that of a normal green compact for sintering, and when a liquid phase is generated by heating, normal liquid phase sintering is performed. Since the surface of aluminum powder is covered with an extremely stable oxide film, the liquid phase must break through the oxide film and flow out of the powder particles in order to generate the liquid phase and perform the function of liquid phase sintering. I won't. In the present invention, avoiding such a situation, positively selecting the condition that the treated product as heated is a defective product as a sintered product, the liquid phase is surrounded by the shell of the oxide film Heat as if it stayed inside. Therefore, the preferable heating temperature is 20 ° C. or more lower than that in normal liquid phase sintering, and is the recrystallization temperature or more for the reason described in the description of the structure.

Thereafter, rolling, extrusion, die pressing or the like is preferably applied to apply a compressive force to the heated support base material and the mixture, thereby breaking the oxide film and allowing the liquid phase to flow out of the powder particles. Further, it is made to flow in the raw material powder. The processing end temperature is preferably within the above-mentioned preferable temperature range so that these phenomena continue to occur during processing. The liquid phase solidifies after processing.

When the aluminum powder is an alloy, since the liquid phase and the solid phase exist in an equilibrium state, the latter is plastically worked at the time of working, the former is fluid and solidifies as it is when the working temperature is within the desired range. When the processing end temperature is lower than the solidus, the latter is plastically processed after flowing. However, even in this case, the characteristic of the fluid structure remains in the product. On the other hand, when the aluminum powder is pure aluminum, the entire inside surrounded by the skin of the oxide film becomes a liquid phase at a temperature slightly higher than the melting point.

As a method different from the above-mentioned preferred manufacturing method, as shown in JP-A-58-153706, the solid phase may be kept as it is and the processing may be carried out in a melted state in which the A1 liquid phase is present. Good. However, it is preferable that substantially all of the above A1 maintains the particle shape and the processing is performed in a state where the inside is in the liquid phase.
It is preferable from the aspect of liquid phase management described later.

The above processing may be performed twice or more. Further, hot or cold working may be performed after the above working. After these processes, semi-molten bonding or hot or cold bonding is performed for bonding with the supporting base material. The processing of the present invention may be performed after the bonding with the supporting base material. Further, heat treatment for the purpose of stress removal of the entire sliding material material, softening of aluminum, precipitation, etc. may be performed during or after these steps. Further, if it is not liquid phase sintering, sintering for increasing the density of the raw material powder may be performed during or after the above steps. This is because when liquid phase sintering is performed before semi-melt processing, the low melting point composition segregates in the secondary phase of the aluminum alloy and the high melting point composition segregates in the matrix phase. This is because the discharge of the liquid phase from the matrix phase particles is hindered, and as a result, the fine distribution of the additive is also hindered, which is not preferable.

Liquid phase sintering may be performed after the processing of the present invention is completed. This liquid phase sintering is performed to further increase the density of the product. In this case, since the low melting point composition is segregated in the secondary phase, the secondary phase melts to fill the pores and increase the density. Therefore, the morphology of the solidified phase that has flowed under compression may hardly remain, but it is effective in improving the density.

Now, another manufacturing method of the present invention will be described. First, the above powders are mixed with a V-type blender to obtain a mixture having a predetermined composition, and the predetermined mixture is laminated to a thickness of 3 mm on a commercially available aluminum alloy plate (thickness 2 mm), and then cold rolled by a roll. Roll down at 20%, then 6
The work piece was inserted into a furnace kept at 00 ° C and held for 15 seconds. Immediately thereafter, the processed piece was rolled to a diameter of 300 mm, a rolling load of 500 kgf, a rolling reduction of 30%, and a rolling finish temperature of 450.
Cool at a temperature of ℃ while applying compressive force. Also by this method, the semi-melt processing (that is, the processing in the solid-liquid coexistence state of the aluminum alloy), which is a feature of the present invention, can be performed. This aluminum-based composite material was further placed in a furnace and held under the same temperature conditions for 15 seconds, and then the aluminum plate and the steel plate were immediately cooled by a roll while applying a compressive force to the whole to form a composite sliding material. Obtained. In this processing, semi-melting processing and Al / Fe pressure welding are simultaneously performed. However, in this semi-melt processing, the fluidized and solidified secondary phase produced in the semi-melt processing is mainly re-melted, and the matrix phase is hardly melted. Here, the steel sheet may be heated in the furnace simultaneously with the aluminum-based composite material.

The structure of the composite sliding material thus obtained has the same structure as that of the embodiment of the present invention described above. Here, for the joining of the aluminum-based composite material and the steel sheet, cold rolling or hot rolling may be performed, but in the case of cold rolling, the lubricant tends to be elongated and Compared with the above method, the sliding material tends to be unsatisfactory in performance, and in the case of hot rolling, the aluminum phase of the alloy structure is likely to change due to heating to the processing temperature of iron. Since the performance as is likely to be unsatisfactory, it is very difficult to set the manufacturing conditions at the time of adoption, and it is considerably limited.

FIG. 8 is a schematic view of a manufacturing apparatus for carrying out the above method.
Shown in. The support base material 1 such as a coiled aluminum alloy strip is unwound and receives the mixed powder 2 scattered thereon. These 1, 2 are compressed by roll 3,
It becomes the preforming band 4. The preforming zone 4 is passed through a furnace 5, heated to a semi-melt processing temperature, and semi-melt processed by a roll 6 outside the furnace. As a result, the composite aluminum plate 7 is obtained.

The steel strip 9 unwound from the coil shape, the direction change rolls 10, 11 and 12 are brought close to the composite aluminum strip 8, bent in the same direction and laminated. The steel strip 9 and the composite aluminum plate 7 are heated by a furnace 8 and pressed by a roll 13 outside the furnace. The bearing material 14 composed of the steel plate / aluminum alloy plate / remelted Al layer thus obtained is wound into a coil. By this winding, the aluminum alloy strip 1 and the steel strip 9 are wound up. Here, in order to form the preforming band, instead of forming by the roll 3, provisional sintering may be performed such that the morphology of the particles remains.

A specific example of the semi-melt processing method using the above apparatus will be described. A mixture 2 containing an aluminum alloy powder and a lubricant powder is preformed by a roll 3 into a plate-like material having a thickness of 4 mm so that the particle morphology remains.
A steel plate or the like which is an aluminum-based material or a non-aluminum-based material is prepared as
It was inserted into the furnace 5 kept at 0 ° C. and kept for 15 seconds. Immediately thereafter, the support substrate 1 and the preforming band 4 are rolled to a roll diameter of 30.
Cooling is performed while applying a compressive force under conditions of 0 mm, a rolling load of 500 kgf, and a rolling reduction of 45% under conditions of a roll temperature at which the aluminum-based plate material can be substantially solidified after passing through the roll 6.

Further, as shown in FIG. 9, the mixture 2 containing the lubricant powder is formed into a plate-like material 15 in which the particle form remains by means of a roll 3, and the plate-like material 15 is substantially made of aluminum alloy powder. While maintaining the particle morphology as a whole, the inside of the particles is heated in the heating furnace 5 to a temperature at which the particles melt,
After that, the plate-shaped material may be subjected to a process of cooling while applying a compressive force by the rolls 6, and may further be pressed into contact with a supporting base material made of a steel plate as in FIG.

As shown in FIGS. 10 and 11,
Bearing material 14 after being composited with a supporting base material and wound up
You may make it join a with the other support base material 9 in another line. Although FIG. 11 shows a case where the bearing material 14a is joined to the support base material 9 in the cold pressure welding step, the pressure welding material 14b is used.
For example, it is preferable to apply annealing under the condition of 300 to 400 ° C.

In the production method of the present invention, it is desirable that a large amount of liquid phase does not ooze out on the sliding side surface of the aluminum-based composite material during cooling while applying compressive force. For this purpose, in a kind of transition state in the vicinity of the roll, first, the liquid phase content is 30 to 70 inside the preform.
%, And more preferably 40 to 55%. Next, when the preform comes close to the roll and the compressive force is transmitted to the aluminum powder, the internal liquid phase component is released while being plastically deformed together with the lubricant containing the external solid phase component and the softened internal solid phase component. ,
The liquid phase becomes a form that wraps the lubricant and the like. The liquid phase begins to solidify by the cooling of the roll while being compressed under the roll. After passing through the rolls, the pressure is released, and in the state where heat is radiated from the composite material, recrystallization of the plastically deformed aluminum gradually progresses and internal strain due to rolling is released. If the internal liquid phase is too much in the processing method in which such a state is sequentially passed, a large amount of liquid phase oozes out to the rear side of the roll. The solidification of this bleeding liquid phase on the sliding side surface is a cause of unevenness in the surface and shrinkage cavities, which is not preferable in manufacturing because it increases post-processing of the surface. It also causes internal defects in moving materials. In order to avoid this, it is necessary to balance the heating temperature, the pressurizing pressure, the cooling conditions, etc., and sufficiently control the internal liquid phase.

Further, a composite sliding material is manufactured by subjecting the mixture to a mixture further containing an organic binder, and subjecting the mixture to a binder removal treatment to remove the organic binder from the mixture before performing the processing. You can also Polyvinyl alcohol or the like can be used as the organic binder. By using the organic binder, it is possible to increase the density of the material obtained by molding the raw material powder and enhance the moldability, and it is easy to handle, and it is possible to prevent the powder from scattering when the roll is inserted. However, since the organic binder does not have excellent sliding properties, the binder is removed from the product by heating it at a temperature equal to or higher than its evaporation temperature or by using a suitable solvent until the processing of the present invention is performed. You have to make sure it doesn't remain.

According to the method of the present invention described above, the following features are remarkably recognized. 1) The compression facilitates the destruction of the aluminum oxide film. Specifically, the oxide film can be destroyed with a smaller amount of liquid phase than in liquid phase sintering. 2) According to the above 1), it is possible to use a fine powder having an excellent sinterability (for example, one having an average particle size of 5 μm or less). 3) The liquid phase not only contributes to improvement of sinterability as in liquid phase sintering, but also contributes to fine dispersion of the additive by flowing due to compressive force. 4) The amount of processing of the aluminum matrix phase is larger in the processing performed at the solid-liquid coexisting temperature than in the simple plastic processing performed at the temperature at which the liquid phase does not occur. For this reason, the surface area of the aluminum powder is increased, and along with this, the lump of the additive is also divided.

Even if the additive is stretchable and soft, since the additive does not melt at the processing temperature, the amount of deformation of the aluminum powder is larger than that of the additive. Therefore, the additive is not stretched into a fibrous shape, and the aluminum alloy is largely deformed. However, the low melting point metal such as Pb is once melted by heating to the processing temperature and then redispersed in a lump form.

[0044]

The sliding material of the present invention has improved wear resistance due to an increase in the binding force of the matrix powder and an increase in the adhesion of the additive to the matrix. Further, the uniform dispersion of the lubricant additive improves the seizure resistance. Further, since the stretchable additive does not significantly spread, the abrasion resistance does not deteriorate due to the peeling.

Further, according to the method of the present invention, it is possible to improve the wear resistance and the seizure resistance by increasing the composite amount of the additive and by using the fine particles. Further, if the characteristics are the same, coarse aluminum powder can be used.
Hereinafter, the present invention will be described in detail with reference to examples.

[0046]

EXAMPLE The treatment of the present invention was carried out using three kinds of raw material powders shown in Table 1.

[0047]

[Table 1]

First, the above powders were mixed with a V-type blender, and the mixture was laminated to a thickness of 3 mm on a commercially available aluminum alloy plate (thickness: 2 mm), and then rolled by a roll at a reduction rate of 20%. Then, the work piece was placed in a furnace kept at 600 ° C. and kept for 15 seconds. Immediately thereafter, the workpiece is cooled under a condition of a roll diameter of 300 mm, a rolling load of 500 kgf, a rolling reduction of 30%, and a rolling finish temperature of 450 ° C. while applying a compressive force. Processing in a solid-liquid coexisting state) was performed. The resulting composite material had a density of 96%.

As a comparative example, a practical aluminum casting alloy (Al-3Si-1Cu-13Sn-) having excellent seizure resistance was used.
2Pb-0.2Cr) was used as comparison A. A seizure resistance test was conducted under the following conditions. Seizure resistance test (test condition A) Tester: High-speed load thrust tester (3-pin desk type) Sliding speed: 4m / s Load: 30kgf / 30min increase every 15 minutes Oil type: Light oil disc: S55C Quenched and tempered material (hardness: Hv500) Pin: Test material As shown in Table 1, the composite sliding material of the present invention has excellent seizure resistance as compared with Comparative A.

Next, the treatment of the present invention was carried out using eight kinds of raw material powders shown in Table 2. Comparative B and Comparative C are shown in Table 2
3 is a comparative example of liquid phase sintering in which the raw material powder of (1) was sintered at 620 ° C. × 1 Hr in nitrogen gas, and then joined to a backing steel plate by cold rolling. Comparative D is a comparative example corresponding to JP-A-58-153706 in which a raw material powder containing only hard particles was used without adding a lubricant having stretchability. Atomized Pb powder (average particle size 40 μm) was used as Pb of the present invention products 4, 5, 7, and 8. In the product 10 of the present invention,
Al-Pb alloy powder was used.

[0051]

[Table 2]

[0052]

[Table 2] Continuation

Seizure resistance test Testing machine: High-speed load thrust tester (3-pin desk type) Sliding speed: 5m / s Load: Increases every 15 minutes at a rate of 33 kgf / 15 min Oil type: Christol # 50 (5cc / min) Pin: SUJ2 (surface roughness 0.8 ± 0.1 μm Rz) Disc: sample

Abrasion resistance tester: Cylindrical flat plate type / friction and wear tester Sliding speed: 0.5 m / s Sliding distance: 3780 m Load: 33 kgf and 9 kgf Oil type: Kerosene shaft: S55C hardened material (surface roughness 0.8-0.9 μmR
z)

The structure of the sample of the product 6 of the present invention is shown in FIG. In the figure, the black flake structure is graphite, the white spherical structure is alumina, some crystal grains are found in the matrix aluminum phase, and the net-like phase covering the matrix phase is solidified under compression. It is a secondary phase.

In Comparative Material B, shearing occurred in the stretched portion of graphite and many cracks were generated in the composite layer, and seizure resistance and wear resistance could not be measured.

The structure of the sample of comparative material C is shown in FIG. In the figure, the black flaky structure is elongated in a very long way by graphite, and the fluidized and solidified secondary phase of aluminum is not observed. For this reason, seizure resistance and wear resistance are inferior to the products of the present invention, and in addition, in the sample of Comparative C, fatigue peeling easily occurs in a very elongated stretched portion of the structure. And, as shown in Table 2, the composite sliding material of the present invention has excellent seizure resistance and abrasion resistance as compared with Comparative D.

Next, another embodiment of the present invention will be described. The same process as in Example 1 was carried out by changing the amount of atomized Pb powder (average particle size 40 μm) in the product 7 of the present invention in Table 2 to 10% by volume. A photograph of the structure of the sliding layer is shown in FIG. In the figure, the white spherical structure is alumina, some crystal grains are recognized as the matrix aluminum phase, and the matrix phase covering the matrix phase is the aluminum secondary phase solidified under compression. A black coarse-grained stretched structure is Pb that is solidified and solidified while being rolled in a liquid state. The composite sliding material thus formed was superior in seizure resistance to the product 7 of the present invention.

Also, in the product 7 of the present invention, the aluminum powder used was changed to Al-3Si-3Cu, and Al-1C was used.
Various aluminum alloy powders such as u, Al-1Si, and Al-5Si-1Cu were treated in the same manner as in Example 1 described above. As a result, seizure resistance or wear resistance was equivalent to or higher than that of the other products of the present invention. Compared with the case where no addition is made, the component range in which a more preferable performance improving effect is obtained is 0.1 to 10% for Cu, more preferably 1 to 5%, 1 to 8% for Si and 0 for Mg. 0.1 to 5%, and Mn, Mo, and Cr were 0.01 to 3%, respectively. You may mix | blend below these lower limit values if desired.

[0060]

The aluminum-based composite sliding material provided by the present invention can meet severe sliding conditions such as high load, high speed, and small amount of oil.

[Brief description of drawings]

FIG. 1 is a diagram showing a schematic structure of a sliding layer of a sliding material according to the present invention.

FIG. 2 is a diagram showing a schematic structure of a sliding layer of a sliding material according to a conventional liquid phase sintering method.

FIG. 3 is a diagram showing a schematic structure of a sliding layer of a conventional sliding material according to a stretch method.

FIG. 4 is a diagram schematically showing the shape of raw material powder.

5 is a schematic diagram of No. 1 of Embodiment 1 of the present invention. 6 is a micrograph of No. 6.

FIG. 6 is a micrograph of another example of the present invention.

FIG. 7 is a micrograph of a sample material of Comparative C.

FIG. 8 is a diagram showing an outline of a manufacturing method according to the present invention.

FIG. 9 is a diagram showing an outline of another manufacturing method according to the present invention.

FIG. 10 is a diagram showing an outline of another manufacturing method according to the present invention.

FIG. 11 is a diagram showing an outline of a further manufacturing method according to the present invention.

[Explanation of symbols]

1 Support substrate (aluminum alloy strip) 2 mixed powder Three rolls 4 Preforming band 5 furnaces 6 rolls 7 Composite aluminum plate 8 furnaces 9 steel strip 14 Bearing material

   ─────────────────────────────────────────────────── ─── Continued front page    (72) Inventor Toshihiko Kira               3-65 Midorigaoka, Toyota City, Aichi Prefecture Otoyo               Industry Co., Ltd. (72) Inventor Souji Kamiya               3-65 Midorigaoka, Toyota City, Aichi Prefecture Otoyo               Industry Co., Ltd.

Claims (11)

(57) [Claims] 1. An aluminum-based composite sliding material in which a sliding layer adhered to a supporting substrate has 1 to 30% by volume of lubricant particles dispersed in an aluminum or aluminum alloy phase, wherein the lubricant particles are An aluminum-based composite sliding material comprising stretchable particles, wherein the aluminum or aluminum alloy phase comprises a secondary phase fluidized and solidified under compression and a recrystallized matrix phase. 2. The aluminum-based composite sliding material according to claim 1, wherein 0.5 to 10% by volume of hard material particles are dispersed in the sliding layer. 3. The aluminum-based composite sliding material according to claim 1, wherein the secondary phase of the aluminum alloy phase is plastically deformed. 4. The supporting base material is an aluminum-based material,
The aluminum-based composite sliding material according to any one of claims 1 to 3, wherein the aluminum-based composite sliding material is selected from the group consisting of non-aluminum-based materials and composite materials thereof. 5. A mixture comprising aluminum or aluminum alloy powder and extendable lubricant powder supported on a supporting substrate, wherein substantially all of said aluminum or aluminum alloy powder maintains a particle morphology and A method for producing an aluminum-based composite sliding material, comprising heating to a temperature at which the inside melts, and then subjecting the supporting base material and the mixture to a compressive force. 6. A mixture comprising aluminum or aluminum alloy powder and extendable lubricant powder is molded into a plate-like material in which the particle morphology remains to prepare a supporting base material, and then the supporting base material and the above-mentioned supporting base material are prepared. The plate-shaped material is heated to a temperature at which substantially all of the aluminum or aluminum alloy powder maintains the particle morphology and the inside of the particles is melted, and then a compressive force is applied to the supporting base material and the plate-shaped material. A method for producing an aluminum-based composite sliding material, which comprises subjecting to processing and cooling. 7. The method for producing an aluminum-based composite sliding material according to claim 5, wherein the supporting base material is an aluminum-based material or a non-aluminum-based material. 8. A support material is prepared by molding a mixture comprising aluminum or aluminum alloy powder and extendable lubricant powder into a plate-like material in which the particle form remains, and then,
The plate-shaped material, while substantially all of the aluminum or aluminum alloy powder maintains the particle morphology, is heated to a temperature at which the inside of the particles melt, and then subjected to a process of applying a compressive force to the plate-shaped material, Further, the method for manufacturing an aluminum-based composite material, characterized in that the plate-shaped material and the supporting base material are brought into pressure contact with each other. 9. The hard particles are further mixed with the mixture containing aluminum or aluminum alloy powder and extendable lubricant powder.
9. The method for manufacturing an aluminum-based composite material according to any one of 1 to 8. 10. The aluminum-based composite material according to claim 5, wherein the mixture is sprayed on the supporting base material, the mixture is pressed down on the supporting base material, and then the heating is performed. Manufacturing method. 11. The method for producing an aluminum-based composite sliding material according to claim 10, wherein the mixed mixture is pre-sintered in addition to or instead of the reduction.