JP6026319B2 - Manufacturing method of sintered bearing - Google Patents

Description

  The present invention relates to a method for manufacturing a sintered bearing having excellent corrosion resistance and wear resistance and high strength.

  Conventionally, for example, motor fuel pumps are used in engines that use gasoline, light oil, or the like as fuel. In recent years, engines equipped with motor-type fuel pumps using fuels such as gasoline and light oil have been widely used in various parts of the world, and the quality of gasoline and light oil used is different in each region of the world. There are many areas where gasoline is used. Gasoline containing organic acids is known as a kind of poor gasoline, but when copper-based sintered bearings are used in motor-type fuel pumps, copper-based sintering is caused by organic acids contained in such bad gasoline. The bearing is corroded. This corrosion progresses to the periphery of the pore opening that opens on the bearing surface and the inner surface of the pore, and further to the inner surface of the pore that exists inside the bearing and communicates from the surface to the inner surface. The life of the copper-based sintered bearing is shortened.

  Furthermore, in recent years, engines such as automobiles have been remarkably reduced in size and weight, and accordingly, fuel pumps are also required to be reduced in size and weight, and sintered bearings incorporated therein are also required to be reduced in size. For example, in a motor-type fuel pump, it is necessary to increase the number of rotations in order to reduce the size while ensuring discharge performance. Accordingly, fuel such as gasoline taken into the fuel pump has a narrow gap flow passage. Under such conditions, the sintered bearing is required to be compact and have higher strength and wear resistance. For this reason, the conventional copper-based sintered bearing has high strength but is not sufficient in terms of wear resistance.

  As a sintered bearing used for such an application, for example, Patent Document 1 discloses a Cu—Ni—Sn—C—P based sintered bearing.

  On the other hand, an aluminum bronze sintered bearing is known as a sintered bearing having excellent mechanical properties and corrosion resistance. In this sintered bearing, there is a problem in that it is not possible to easily obtain a sintered body having sufficient strength for the aluminum oxide covering the surface of the aluminum-containing copper alloy powder produced during sintering to inhibit the sintering. is there. Patent Document 2 discloses a technique relating to a mixed powder for a sintered aluminum-containing copper alloy and a method for producing the same in order to improve the above problem.

Japanese Patent No. 45211871 JP 2009-7650 A

  The Cu—Ni—Sn—C—P based sintered bearing described in Patent Document 1 improves strength and wear resistance, but is not sufficient in terms of corrosion resistance. Further, since Ni which is a rare metal is contained, there is a problem in terms of cost.

  The aluminum-containing copper alloy powder described in Patent Document 2 is excellent in formability and sinterability, but as an aluminum bronze-based sintered bearing using the aluminum-containing copper alloy powder, stable mechanical properties, Further studies are necessary to obtain a product suitable for mass production that satisfies compactness and low cost.

  In view of the conventional problems, an object of the present invention is to provide a method for producing an aluminum bronze sintered bearing that is good in productivity, low in cost, and suitable for mass production.

  As a result of various investigations to achieve the above object, the present inventor has achieved a high productivity, low cost, and suitable manufacturing method for mass production as a manufacturing method of an aluminum bronze sintered bearing. This led to a new idea of effectively utilizing expansion due to sintering.

As a technical means for achieving the above-mentioned object, the present invention contains 3 to 12% by mass of aluminum and 0.05 to 0.5% by mass of phosphorus, with the balance being copper as an inevitable impurity. A method for producing a sintered bearing comprising: a green compact step of forming a green compact obtained by adding a sintering aid to a raw material powder; and an aluminum-copper from the green compact. A sintering process for obtaining a sintered body having a structure in which the alloy is sintered, and a sizing process for sizing the sintered body, wherein a die for the sizing process is formed from a die, a pair of punches, and a core. The inner diameter side of the sintered body is shaped by the core by being compressed from both the axial side and the outer diameter side of the sintered body by the punch and the die, and the inner diameter dimension of the die and the outer diameter of the sintered body are Dimensional difference from the diameter The size of pores on the surface of the sintered body is set by adjusting the difference in size between the outer diameter of the sintered body and the inner diameter of the sintered body. Thereby, it is possible to realize a manufacturing method of an aluminum bronze-based sintered bearing that is good in productivity, low in cost, and suitable for mass production. The sintered bearing thus manufactured can improve mechanical properties such as corrosion resistance, strength, and wear resistance, oil film formation, and oil retention, and can be made compact. The die for the above sizing process is composed of a die, a pair of punches and a core, and the inner diameter side of the sintered body is shaped by the core by compressing the sintered body from both sides in the axial direction and the outer diameter side with the punch and the die. It is preferable to do. Thereby, the expansion | swelling by sintering of an aluminum copper type sintered bearing can be utilized effectively, and a desired pore can be formed with the dimension shaping of a sintered bearing. A method of manufacturing a sintered bearing containing 3 to 12% by mass of aluminum and 0.05 to 0.5% by mass of phosphorus, the remaining main component being copper and containing inevitable impurities, , At least 0.05 to 0.2% by mass in total of aluminum fluoride and calcium fluoride with respect to 100% by mass in total of the aluminum, phosphorus, raw material powder having copper as the main component and the inevitable impurities. In addition, a compacting step of forming a green compact to which 1 to 5% by mass of graphite is added, a sintering step of obtaining a sintered body having a structure in which an aluminum-copper alloy is sintered from the green compact, from particular characterized in that it comprises a sizing step of dimensional shaping a sintered body, good productivity, at low cost, to realize a method of manufacturing a suitable aluminum bronze based sintered bearings mass production Can do. The sintered bearing thus manufactured can improve mechanical properties such as corrosion resistance, strength, and wear resistance, oil film formation, and oil retention, and can be made compact.

  The content of aluminum is preferably 3 to 12% by mass. If the aluminum content is less than 3% by mass, the effects of corrosion resistance and wear resistance as an aluminum bronze sintered bearing cannot be obtained, and the expansion of the sintered body is small. This is not preferable because the strength of the sintered body is reduced and the expansion of the sintered body becomes too large.

  The compounding amount of phosphorus is preferably 0.05 to 0.5% by mass. If it is less than 0.05% by mass, the effect of promoting the sintering between the solid and liquid phases is poor. On the other hand, if it exceeds 0.5% by mass, the sintering proceeds so much that the aluminum is segregated and the precipitation of the γ phase increases. Is not preferable because it becomes brittle. This is an alloy phase of copper and aluminum, and the β phase is transformed into a γ phase at the eutectoid temperature (565 ° C.).

As a sintering aid, a total of 0.05 to 0.2 mass of aluminum fluoride and calcium fluoride with respect to a total of 100 mass% of aluminum, phosphorus, the raw material powder having copper as the main component and the inevitable impurities. By adding%, the aluminum oxide film can be broken by reacting with the aluminum oxide generated at the time of increasing the temperature of sintering to promote the sintering. The total amount of aluminum fluoride and calcium fluoride is preferably 0.05 to 0.2% by mass. If it is less than 0.05% by weight, the effect as a sintering aid is insufficient, and a dense sintered body having an appropriate hardness cannot be obtained. On the other hand, if it exceeds 0.2% by mass, the effect as a sintering aid will reach its peak even if it is added more, and it is preferable to keep it to 0.2% by mass or less from the viewpoint of cost. 1 to 5% by mass of graphite can be added to the total of 100% by mass of the above raw material powder and inevitable impurities. Thereby, it exists as a free graphite in the pores distributed and distributed, and imparts excellent lubricity to the sintered bearing, thereby further improving the wear resistance. The amount of graphite is preferably 1 to 5% by mass. If it is less than 1% by mass, the effect of improving the lubricity and wear resistance by adding graphite cannot be obtained. On the other hand, if it exceeds 5% by mass, the strength decreases, which is not preferable.

When the above aluminum fluoride and calcium fluoride are used as sintering aids, it is preferable that 2 to 4% by mass of zinc is added. Zinc has a low melting point, promotes the sintering of copper and aluminum, and promotes the diffusion of aluminum. Furthermore, it is excellent in corrosion resistance. If the blending amount of zinc is less than 2 % by mass, the effect of promoting the sintering of copper and aluminum and the effect of promoting the diffusion of aluminum cannot be obtained. On the other hand, if it exceeds 4% by mass, zinc evaporates during sintering and the sintering furnace is fouled, and aluminum is segregated and diffusion is hindered.

  Furthermore, it is preferable that 0.5-3 mass% of silicon is added. Silicon generates a copper silicon-based liquid phase for the sintering progress-inhibiting phase formed in the sintering process and promotes the sintering. Since silicon increases the diffusion of aluminum during the sintering process, the amount of aluminum can be reduced and the γ phase can be reduced. The blending amount of silicon is preferably 0.5 to 3% by mass. If it is less than 0.5% by mass, the effect of enhancing the diffusion of aluminum in the sintering process is insufficient, and accordingly, the effect of reducing the γ phase becomes insufficient. On the other hand, if it exceeds 3% by mass, silicon reacts when the temperature rises during sintering, and aluminum is oxidized black, resulting in a discoloration defect.

It is preferable that the copper raw material powder is mainly composed of electrolytic copper powder . Since the electrolytic copper powder has a dendritic shape, aluminum can be sufficiently diffused into copper, and the moldability, sinterability, and sliding properties are excellent.

By applying a mesh belt type continuous furnace to the above-mentioned sintering process, further improvement in productivity and cost reduction can be achieved, and sufficient strength can be secured in terms of the function of the sintered bearing. Specifically, the load of the mesh belt type continuous furnace is reduced by setting the sintering temperature in the sintering step to 850 to 950 ° C., the sintering atmosphere to be a reducing atmosphere, and the sintering time to be 10 to 60 minutes. Stable quality, manufacturing method can be realized.

  By adjusting the dimensional difference between the inner diameter dimension of the die and the outer diameter dimension of the sintered body and the dimensional difference between the outer diameter dimension of the core and the inner diameter dimension of the sintered body, the pore size on the surface of the sintered body is increased. Can be set. Thereby, the size of the pores on the surface of the sintered bearing can be easily controlled.

  According to the present invention, it is possible to realize a method for producing an aluminum bronze-based sintered bearing that is good in productivity, low in cost, and suitable for mass production. Moreover, the sintered bearing based on the manufacturing method of this invention can improve mechanical characteristics, such as corrosion resistance and intensity | strength, abrasion resistance, oil film formation property, and oil retention.

It is sectional drawing of the sintered bearing based on the manufacturing method which concerns on the 1st-3rd embodiment of this invention. It is the schematic diagram which expanded the metal structure of the said sintered bearing. It is a figure explaining the process of the manufacturing method which concerns on the 1st Embodiment and 2nd Embodiment of this invention. It is a schematic diagram of the raw material powder mixer. It is a schematic diagram of a mesh belt type continuous furnace. It is a figure explaining a sizing process. It is a figure which shows the compression state of the product in a sizing process. It is a schematic diagram of an oil impregnation apparatus. It is a longitudinal cross-sectional view of a fuel pump.

  DESCRIPTION OF EXEMPLARY EMBODIMENTS Hereinafter, a first embodiment of the invention will be described with reference to the accompanying drawings. A manufacturing method according to the first embodiment of the present invention is shown in FIGS. 3 to 8, and a sintered bearing based on this manufacturing method is shown in FIGS. First, the sintered bearing based on this manufacturing method is demonstrated based on FIG. 1 and FIG. 2, and a manufacturing method is demonstrated based on FIGS.

  As shown in FIG. 1, the sintered bearing 1 is formed in a cylindrical shape having a bearing surface 1a on the inner periphery. When the shaft 2 is inserted into the inner periphery of the sintered bearing 1 and the shaft 2 is rotated in that state, the lubricating oil retained in the countless holes of the sintered bearing 1 oozes into the bearing surface 1a as the temperature rises. put out. The oil that has oozed out forms an oil film in the bearing gap between the outer peripheral surface of the shaft 2 and the bearing surface 1 a, and the shaft 2 is supported by the bearing 1 so as to be relatively rotatable.

  The sintered bearing 1 is formed by filling a raw material powder mixed with various powders into a mold, compressing this to form a green compact, and then sintering the green compact.

  The raw material powder is a mixed powder mainly composed of copper powder, powder composed of copper, aluminum, and aluminum-copper alloy, silicon powder, tin powder, phosphorus alloy powder, and graphite powder. Details of each powder are described below.

[Copper powder]
As the copper powder, spherical or dendritic copper powder that is widely used for sintered bearings can be used. For example, reduced powder, electrolytic powder, water atomized powder, and the like are used. The particle size is 100 mesh passing powder and 350 mesh passing powder ratio is 40% or less.

[Powder composed of copper, aluminum and aluminum copper alloy composition]
40% to 60% by mass of aluminum powder and the remaining powder mixed with copper powder are heat-treated in a reducing or inert atmosphere and then pulverized to adjust the particle size, and the powder composed of copper, aluminum and aluminum copper alloy composition An aluminum-copper alloy powder). The preferable particle size of the aluminum-copper alloy powder is 80 mesh passing powder and 350 mesh passing powder ratio is 60% or less. By using the aluminum-copper alloy powder, the problem of insufficient strength of the green compact due to the decrease in formability due to the hardness of the powder is improved, and there is no problem in handling due to scattering of single aluminum particles having a small specific gravity. .

  The composition of the aluminum-copper alloy powder is preferably in the range of 40-60 mass% aluminum. Powder containing aluminum of less than 40% by mass is a copper-silicon liquid phase under low-temperature sintering due to a reduction in green compact density during pressure forming due to a decrease in the copper powder mixing ratio and an alloy phase with a high melting point. The generation amount is reduced, and the effect of adding the sintering promoting element is reduced. On the other hand, in the powder containing aluminum exceeding 60% by mass, the unreacted aluminum particles are scattered due to the increase of the copper particles and the unreacted aluminum particles, which causes a problem in handling.

  In this embodiment, the aluminum content is 3 to 10% by mass, silicon is 1 to 4% by mass, tin is 0.5 to 2% by mass and phosphorus is 0.05 to 0.5% by mass, and the remaining main components Are mixed in a ratio such that copper becomes copper, aluminum-copper alloy powder, and phosphorus alloy powder, silicon powder, and tin powder, which will be described later, and the total amount of graphite is 1 to 100% by mass. Graphite powder is mixed so as to be 5% by mass to obtain a raw material powder.

[Phosphorus alloy powder]
Phosphorous improves the wettability between the solid and liquid phases during sintering, and suppresses the formation of a nitride film that shifts the liquid phase generation temperature caused by the addition of silicon powder to the low temperature side. The compounding amount of phosphorus is preferably 0.05 to 0.5% by mass. If it is less than 0.05% by mass, the effect of promoting the sintering between the solid and liquid phases is poor. On the other hand, if it exceeds 0.5% by mass, the sintering proceeds so much that the aluminum segregates and the γ phase increases and the sintered body becomes brittle. .

[Silicon powder]
Silicon is added as a sintering aid. Silicon generates a copper silicon-based liquid phase for the sintering progress-inhibiting phase formed in the sintering process and promotes the sintering. As for the compounding quantity of silicon, 1-4 mass% is preferable. If the amount is less than 1% by mass, the amount of generated liquid phase is small, and the effect of promoting liquid phase sintering at low temperatures becomes insufficient, and a dense sintered body having an appropriate hardness cannot be obtained. On the other hand, if it exceeds 4% by mass, the sintering proceeds too much, so that aluminum is segregated and the γ phase increases and the sintered body becomes brittle.

[Tin powder]
Tin is added as a sintering aid. Tin compensates for the decrease in moldability associated with the addition of silicon powder, and has the effect of lowering the liquid phase generation temperature produced by the addition of silicon powder, as with phosphorus. As for the compounding quantity of tin, 0.5-2 mass% is preferable. If the amount is less than 0.5% by mass, the powder density cannot be increased by adding tin powder. On the other hand, if the amount exceeds 2% by mass, high-concentration tin is precipitated at the grain boundaries, resulting in a deterioration in the appearance quality of the sintered body. This is undesirable.

[Graphite powder]
Graphite exists mainly as free graphite in pores dispersed and distributed in the base material, imparts excellent lubricity to the sintered bearing, and contributes to improvement of wear resistance. As for the compounding quantity of graphite, 1-5 mass% is preferable with respect to a total of 100 mass% of aluminum, silicon, tin, phosphorus, copper, and an unavoidable impurity. If it is less than 1% by mass, the effect of improving the lubricity and wear resistance by adding graphite cannot be obtained. On the other hand, if it exceeds 5% by mass, the strength decreases, which is not preferable.

  FIG. 2 shows a schematic diagram of the metal structure of the cross section of the sintered bearing. FIG. 2A is an enlarged view of part A in FIG. Similarly, FIG. 2B is an enlarged view of the portion B in FIG. 1, and FIG. 2C is an enlarged view of the portion C in FIG. 2A shows the metal structure of the surface layer portion of the bearing surface on the inner diameter side, FIG. 2B shows the metal structure of the inner surface, and FIG. 2C shows the metal structure of the surface layer portion of the outer diameter surface. Indicates. As shown in FIGS. 2A, 2B, and 2C, hatched 3 is an aluminum-copper alloy structure, and an aluminum oxide film 4 exists around the surface and internal pores. For this reason, it is excellent in corrosion resistance and abrasion resistance. Although illustration is omitted, the grain boundary portion of the aluminum-copper alloy structure 3 contains a lot of tin and phosphorus, and silicon is scattered. Since the free graphite 5 is distributed in the pores, it is excellent in lubricity and wear resistance.

  As shown in FIG. 2 (a), an open hole db1 formed on the bearing surface on the inner diameter side and an internal hole db2 on the surface layer of the bearing surface are formed. As shown in FIG. 2 (b), pores di are formed inside the bearing. As shown in FIG. 2 (c), open pores do1 formed on the outer diameter surface and internal pores formed on the surface layer of the outer diameter surface. do2 is formed. The open pore db1 formed on the bearing surface, the internal pore db2 on the surface of the bearing surface, the pore di inside the bearing, the release pore do1 formed on the outer diameter surface, and the internal pore do2 formed on the outer surface of the outer diameter surface are: Each communicates.

  The sintered bearing 1 is sized in the outer diameter surface 1b and the inner diameter side bearing surface 1a of the bearing after sintering in a manufacturing method (see FIG. 7) described later. Since the aluminum bronze-based sintered bearing expands by sintering, the outer diameter surface 1b of the bearing is sized in a larger amount than the bearing surface 1a on the inner diameter side. Therefore, the pores do (see FIG. 2C) of the surface layer portion on the outer diameter surface 1b side are crushed more than the pores db (see FIG. 2A) of the surface layer portion on the bearing surface 1a side. Comparing the sizes of the pores do in the surface layer portion on the outer diameter surface 1b side, the pores db in the surface layer portion on the bearing surface 1a side, and the pores di (see FIG. 2B) inside the bearing that are not crushed, do <db <di It becomes a relationship. Because of this relationship, the bearing surface 1a side can improve the corrosion resistance and oil film formation, while the outer surface 1b side and the end surface 1c side close to the sealed state have corrosion resistance and oil retention. Can be improved.

  Lubricating oil is impregnated in the pores do, db, and di of the sintered bearing 1. Thereby, a better lubrication state can be obtained than at the start of operation. As the lubricating oil, mineral oil, polyalphaolefin (PAO), ester, liquid grease, and the like can be used. However, it is not always necessary to impregnate the lubricating oil for the intended use of the bearing.

  FIG. 1 shows the surface compression layer of the sintered bearing 1 by hatching. Hatching is given only to the upper half of the bearing 1 in the radial direction, and the lower half is not shown. The surface layer of the sintered bearing 1 has a compression layer. The density ratio αo of the outer compression surface Po on the outer diameter surface 1b side and the density ratio αb of the outer compression layer Pb on the bearing surface 1a side are both higher than the internal density ratio αi, and both density ratios αo and αb are present. Are set in the ranges of 80% ≦ αo and αb ≦ 95%. If the density ratios αo and αb are less than 80%, the bearing strength is insufficient. On the other hand, if it exceeds 95%, the oil content is insufficient, which is not preferable. In this specification, αo and αb are collectively referred to as α.

The average value of the depth of the compression layer Po of the surface layer on the outer diameter surface 1b side is To, the average value of the depth of the compression layer Pb of the surface layer on the bearing surface 1a side is Tb, and the inner diameter dimension D1 of the bearing surface When the ratios are To / D1 and Tb / D1, respectively, it is preferable to set 1/100 ≦ To / D1 and Tb / D1 ≦ 1/15. Here, the density ratio α is expressed by the following equation.
α (%) = (ρ1 / ρ0) × 100
However, ρ1: the density of the porous body, ρ0: the density To / D1 and Tb / D1 when the porous body is assumed to have no pores are less than 1/100, the collapse of the pores is insufficient, If it exceeds 1/15, the pores are too crushed, which is not preferable. In this specification, To and Tb are collectively referred to as T.

  Next, the manufacturing method of the sintered bearing which is the 1st Embodiment of this invention is demonstrated. It is manufactured through a raw material powder preparation step S1, a compacting step S2, a sintering step S3, a sizing step S4, and an oil impregnation step S5 as shown in FIG.

[Raw material powder preparation step S1]
In the raw material powder preparation step S1, the raw material powder of the sintered bearing 1 is prepared and generated. The raw material powder was 81% by mass of copper powder, 12% by mass of 50% by mass aluminum-copper alloy powder, 3% by mass of silicon powder, 1% by mass of tin powder, 3% by mass of phosphorus-copper alloy powder. 3 mass% of graphite powder and 0.5 mass% of a lubricant such as zinc stearate and calcium stearate were added to facilitate moldability. By adding the lubricant, it is possible to smoothly release the green compact described later, and to avoid the collapse of the shape of the green compact accompanying the release. Specifically, for example, the raw material powder M is charged into the can body 11 of the V-type mixer 10 shown in FIG. 4, and the can body 11 is rotated and mixed uniformly.

[Green compaction process S2]
In the compacting step S2, a compact 1 '(see FIG. 7) having the shape of the sintered bearing 1 is formed by compacting the raw material powder. The green compact 1 ′ is compression molded so that the density ratio α of the sintered body 1 ″ formed by heating at a sintering temperature or higher is 70% or more and 80% or less. In FIG. In particular, the green compact is labeled 1 'and the sintered body is labeled 1 ".

  Specifically, for example, a molding die that defines a cavity that follows the shape of a green compact is set in a CNC press machine that uses a servo motor as a drive source, and the above-described raw material powder filled in the cavity is 200 to The green compact 1 ′ is formed by compressing with a pressure of 700 MPa. When molding the green compact 1 ′, the molding die may be heated to 70 ° C. or higher.

  In the method for manufacturing the sintered bearing 1 according to the present embodiment, by using aluminum copper alloy powder as the aluminum source, the problem of insufficient strength of the green compact due to a decrease in formability due to fluidity is improved. There are no handling problems associated with the scattering of small aluminum particles. In addition, it has good production efficiency and is suitable for mass production.

[Sintering step S3]
In the sintering step S3, the green compact 1 ′ is heated at a sintering temperature to sinter-bond adjacent raw material powders to form a sintered body 1 ″. A mesh belt type continuous furnace 15 shown in FIG. In order to prevent the oxidation as much as possible, in order to prevent the oxidation as much as possible, a reducing gas atmosphere or a mixed gas atmosphere of hydrogen gas or a nitrogen gas atmosphere is used. Then, the green compact 1 ′ is heated at 850 to 950 ° C. (for example, 900 ° C.) for 10 to 60 minutes to form a sintered body 1 ″. Thereby, the load of a mesh belt type continuous furnace is reduced, and stable quality and a manufacturing method can be realized.

  The aluminum-copper alloy powder generates various liquid phases when the eutectic temperature is 548 ° C. or higher. When the liquid phase is generated, the liquid phase expands, and a sintered neck is formed by the generated liquid phase, leading to densification and shrinking of dimensions. In the present embodiment, by sintering in the mesh belt type continuous furnace 15, the surface of the sintered body 1 "is oxidized, and the size is kept expanded without being densified by inhibiting the sintering. However, since the inside of the sintered body 1 "is sintered without being oxidized, the strength of the sintered body 1" can be sufficiently secured. Since the mesh belt type continuous furnace 15 is used, the green compact is used. Sintering time can be shortened and mass-produced from 1 'input to take-out, cost can be reduced, and sufficient strength can be secured in terms of the function of the sintered bearing.

  In the above sintering step, the added phosphorus alloy powder, tin powder, silicon powder, and graphite powder exhibit a synergistic effect described below, whereby a high-quality sintered body can be formed. First, phosphorus has the effect of increasing the wettability between the solid and liquid phases during sintering and shifting the liquid phase generation temperature generated by the addition of silicon powder to the low temperature side, so that a good sintered body can be obtained. As a compounding quantity of phosphorus, 0.05-0.5 mass% is preferable. If it is less than 0.05% by mass, the effect of promoting the sintering between the solid and liquid phases is poor, whereas if it exceeds 0.5% by mass, the obtained sintered body becomes brittle. Moreover, silicon as a sintering aid generates a copper silicon-based liquid phase and promotes sintering with respect to the sintering progress-inhibiting phase formed in the sintering process. As for the compounding quantity of silicon, 1-4 mass% is preferable. If the amount is less than 1% by mass, the amount of generated liquid phase is small, and the effect of promoting liquid phase sintering at low temperatures becomes insufficient, and a dense sintered body having an appropriate hardness cannot be obtained. On the other hand, when it exceeds 4 mass%, the obtained sintered body becomes hard and brittle.

  In addition, tin as a sintering aid compensates for the decrease in formability associated with the addition of silicon powder, and also exhibits the effect of lowering the liquid phase generation temperature generated by the addition of silicon powder in the same manner as phosphorus. As for the compounding quantity of tin, 0.5-2 mass% is preferable. If the amount is less than 0.5% by mass, the effect of increasing the density of the compacted powder due to the addition of tin powder cannot be obtained. On the other hand, if the amount exceeds 2% by mass, a high concentration of tin precipitates at the grain boundaries, which is not preferable because it inhibits aluminum diffusion. .

  Since the sintering aid is added to the raw material powder M as described above, a sintered body 1 ″ having a structure in which an aluminum-copper alloy is sintered can be obtained, and the strength and corrosion resistance are improved. be able to.

  Further, graphite is present as free graphite mainly in pores dispersed and distributed in the base material, imparts excellent lubricity to the sintered bearing, and contributes to improvement of wear resistance. As for the compounding quantity of graphite, 1-5 mass% is preferable with respect to a total of 100 mass% of aluminum, silicon, tin, phosphorus, copper, and an unavoidable impurity. If it is less than 1% by mass, the effect of improving the lubricity and wear resistance by adding graphite powder cannot be obtained. On the other hand, if it exceeds 5% by mass, the strength decreases, which is not preferable.

[Sizing Step S4]
In the sizing step S4, the sintered body 1 '' expanded as compared with the green compact 1 ′ by sintering is dimensionally shaped. FIG. 6 shows details of the sizing step S4. The upper punch 21, the lower punch 22, and the core 23. As shown in FIG. 6A, the sintered body 1 "is set on the lower punch 22 with the core 23 and the upper punch 21 retracted upward. To do. As shown in FIG. 6B, the core 23 first enters the inner diameter of the sintered body 1 ″, and then the upper body 21 turns the sintered body 1 ″ into the die 20 as shown in FIG. 6C. It is pushed in and compressed by the upper and lower punches 21 and 22. Thereby, the surface of the sintered body 1 ″ is dimensionally shaped. By the sizing process, pores in the surface layer of the expanded sintered body 1 ″ are crushed, and a density difference is generated between the inside of the product and the surface layer portion.

  FIG. 7 shows a state in which the sintered body 1 ″ is compressed by sizing. The sintered body 1 ″ before sizing is indicated by a two-dot chain line, and the product 1 after sizing is indicated by a solid line. As indicated by a two-dot chain line, the sintered body 1 ″ expands in the radial direction and the width direction. For this reason, the sintered body 1 ″ compresses the outer diameter surface 1b more than the bearing surface 1a on the inner diameter side. The As a result, the surface layer pores do (see FIG. 2C) on the outer diameter surface 1b side are crushed more than the surface layer pores db (see FIG. 2A) on the inner diameter side bearing surface 1b, and are not crushed. The relationship is do <db <di with respect to the pore di (see FIG. 2B) inside the bearing. Because of this relationship, the bearing surface 1a on the inner diameter side can improve the corrosion resistance and oil film formation. On the other hand, the outer diameter surface 1b and the end surface 1c close to the sealed state can improve the corrosion resistance and oil retention.

  A die for the above sizing process is composed of a die 20, a pair of punches 21, 22 and a core 23, and is compressed from both sides in the axial direction and the outer diameter side of the sintered body 1 '' by the punches 21, 22 and the die 20. By shaping the inner diameter side of the sintered body 1 ″ with the core 23, it is possible to effectively utilize the expansion caused by sintering of the aluminum bronze sintered bearing and form the desired pores together with the dimension shaping of the sintered bearing 1. it can.

  Further, by adjusting the dimensional difference between the inner diameter dimension of the die 20 and the outer diameter dimension of the sintered body 1 ″ and the dimensional difference between the outer diameter dimension of the core 23 and the inner diameter dimension of the sintered body 1 ″, The size of the pores on the surface of the bonded body 1 ″ can be set. Thereby, the size of the pores on the surface of the sintered bearing 1 can be easily controlled.

[Oil impregnation step S5]
The oil impregnation step S5 is a step in which the product 1 (sintered bearing) is impregnated with lubricating oil. FIG. 8 shows an oil retaining device. The product 1 is put into the tank 26 of the oil impregnating device 25, and then the lubricating oil 27 is injected into the tank 26. Then, by reducing the pressure in the tank 26, the lubricating oil 27 is impregnated in the pores do, db, di (see FIG. 2) of the product 1. Thereby, a better lubrication state can be obtained than at the start of operation. As the lubricating oil, mineral oil, polyalphaolefin (PAO), ester, liquid grease, and the like can be used. However, it is not always necessary to impregnate the lubricating oil for the intended use of the bearing. Therefore, oil impregnation process S6 should just be implemented as needed, and does not necessarily need to implement.

  The manufacturing method of the present embodiment includes the above-described steps, and can realize a manufacturing method of a sintered bearing suitable for mass production with good productivity, low cost, and low cost. In addition, the sintered bearing based on the manufacturing method of the present embodiment can improve mechanical properties such as corrosion resistance and strength, wear resistance, oil film formation, and oil retention.

  Next, the manufacturing method of the sintered bearing which concerns on the 2nd Embodiment of this invention is demonstrated. Whereas the sintering aid added to the raw material powder M in the first embodiment is silicon and tin, the present embodiment is different in that the sintering aid is aluminum fluoride and calcium fluoride.

  The raw material powder in the manufacturing method of the present embodiment is prepared by adding aluminum fluoride and calcium fluoride as sintering aids to the copper powder, aluminum-copper alloy powder, phosphorus alloy powder and graphite powder used in the first embodiment. It is a mixed powder with the main component. Since the contents of the copper powder, the aluminum-copper alloy powder, the phosphorus alloy powder, and the graphite powder are the same as those in the first embodiment, a duplicate description is omitted.

  In the manufacturing method of the second embodiment, the aluminum content is 7 to 12% by mass, the phosphorus is 0.05 to 0.5% by mass, and the remaining main component is copper, and the copper powder, Aluminum-copper alloy powder and phosphorus alloy powder are mixed, and 0.05 to 0.2% by mass in total of aluminum fluoride and calcium fluoride as a sintering aid are added to 100% by mass in total, and graphite is added. 1-5 mass% is mixed and it is set as raw material powder.

[Aluminum fluoride and calcium fluoride]
The aluminum-containing copper-based alloy powder has an aluminum oxide film formed on its surface during sintering that significantly inhibits the sintering, but aluminum fluoride and calcium fluoride as sintering aids are aluminum-containing copper-based alloy powders. It gradually evaporates while melting at a sintering temperature of 850 to 900 ° C., and protects the surface of the aluminum-containing copper-based alloy powder to suppress the formation of aluminum oxide, thereby promoting sintering and diffusion of aluminum. Improve. Aluminum fluoride and calcium fluoride evaporate and volatilize during sintering, and therefore hardly remain in the finished product of the sintered bearing.

  Aluminum fluoride and calcium fluoride as a sintering aid are 0.05 to 0.2 in total with respect to a total of 100% by mass of aluminum, phosphorus, the raw material powder having copper as the main component and the inevitable impurities. It is preferable to add at about mass%. If it is less than 0.05% by weight, the effect as a sintering aid is insufficient, and a dense sintered body having an appropriate hardness cannot be obtained. On the other hand, if it exceeds 0.2% by mass, the effect as a sintering aid will reach its peak even if it is added more, and it is preferable to keep it to 0.2% by mass or less from the viewpoint of cost.

  Since the metal structure of the cross section of the sintered bearing based on the manufacturing method of this embodiment is the same as that of the first embodiment shown in the schematic diagram of FIG. 2, only the main part will be described, and the other parts will be described. Duplicate explanation is omitted. As shown in FIGS. 2 (a), (b), and (c), the sintered bearing 1 based on the manufacturing method of the present embodiment has a hatched 3 aluminum-copper alloy structure, and has surface and internal pores. There is an aluminum oxide film 4 around. For this reason, it is excellent in corrosion resistance and abrasion resistance. Although illustration is omitted, phosphorus exists in the grain boundary portion of the aluminum-copper alloy structure 3. Since the free graphite 5 is distributed in the pores, it is excellent in lubricity and wear resistance.

  Also in the sintered bearing 1 based on the manufacturing method of the present embodiment, as shown in FIG. 7, both the outer diameter surface 1b and the inner bearing surface 1a of the bearing are sized after sintering. And since an aluminum copper series sintered bearing expand | swells by sintering, the outer-diameter surface 1b of a bearing is sized in a bigger quantity than the bearing surface 1a of an internal diameter side. Therefore, the pores do (see FIG. 2C) of the surface layer portion on the outer diameter surface 1b side are crushed more than the pores db (see FIG. 2A) of the surface layer portion on the bearing surface 1a side. Comparing the sizes of the pores do in the surface layer portion on the outer diameter surface 1b side, the pores db in the surface layer portion on the bearing surface 1a side, and the pores di (see FIG. 2B) inside the bearing that are not crushed, do <db <di It becomes a relationship. Because of this relationship, the bearing surface 1a side can improve the corrosion resistance and oil film formation, while the outer surface 1b side and the end surface 1c side close to the sealed state have corrosion resistance and oil retention. Can be improved. Lubricating oil is impregnated in the pores do, db, and di of the sintered bearing 1. Thereby, a better lubrication state can be obtained than at the start of operation. As the lubricating oil, mineral oil, polyalphaolefin (PAO), ester, liquid grease, and the like can be used. However, it is not always necessary to impregnate the lubricating oil for the intended use of the bearing.

  Furthermore, the state of the compression layer of the surface layer of the sintered bearing 1 based on the manufacturing method of the second embodiment is the same as that of the first embodiment shown in FIG. That is, also in the sintered bearing 1 based on the manufacturing method of this embodiment, as shown in FIG. 1, the surface layer of the sintered bearing 1 has a compression layer with hatching. Expressed by the above-described equation of density ratio α, the density ratio αo of the surface compression layer Po on the outer diameter surface 1b side and the density ratio αb of the surface compression layer Pb on the bearing surface 1a side are both internal density ratio αi. The density ratios αo and αb are both set in the ranges of 80% ≦ αo and αb ≦ 95%.

  The average value of the depth of the compression layer Po of the surface layer on the outer diameter surface 1b side is To, the average value of the depth of the compression layer Pb of the surface layer on the bearing surface 1a side is Tb, and the inner diameter dimension D1 of the bearing surface If the ratios are To / D1 and Tb / D1, respectively, they are set to 1/100 ≦ To / D1 and Tb / D1 ≦ 1/15.

  Since the manufacturing process of the second embodiment is the same as that of the first embodiment shown in FIG. 3, only the differences in the specific contents of the raw material powder preparation process S1 and the sintering process S3 will be described.

[Raw material powder preparation step S1]
The raw material powder is based on 100% by mass of copper powder remaining mass%, 40-60% by mass aluminum-copper alloy powder 14-20% by mass, and 8% by mass phosphorous-copper alloy powder 2-4% by mass. As a sintering aid, a total of 0.05 to 0.2% by mass of aluminum fluoride and calcium fluoride, 1 to 5% by mass of graphite powder, zinc stearate, 0.5% by mass of a lubricant such as calcium phosphate was added.

[Sintering step S3]
In the sintering step, the added phosphorus alloy powder, aluminum fluoride, and calcium fluoride exhibit the effects described below, whereby a high-quality sintered body can be formed. First, since phosphorus has an effect of improving the wettability between the solid and liquid phases during sintering, a good sintered body can be obtained. As a compounding quantity of phosphorus, 0.05-0.5 mass% is preferable. If it is less than 0.05% by mass, the effect of promoting the sintering between the solid and liquid phases is poor, whereas if it exceeds 0.5% by mass, the obtained sintered body becomes brittle. In addition, aluminum fluoride and calcium fluoride as sintering aids gradually evaporate while melting at 850 to 900 ° C. which is the sintering temperature of the aluminum-containing copper-based alloy powder, and the surface of the aluminum-containing copper-based alloy powder Sintering is enabled by protecting the formation of aluminum oxide and protecting aluminum. Aluminum fluoride and calcium fluoride evaporate and volatilize during sintering, and therefore hardly remain in the finished product of the sintered bearing. Since it evaporates and volatilizes, the green compact is placed in a case or the like and sintered. Aluminum fluoride and calcium fluoride as a sintering aid are 0.05 to 0.2 in total with respect to a total of 100% by mass of aluminum, phosphorus, the raw material powder having copper as the main component and the inevitable impurities. It is preferable to add at about mass%.

  Also in the present embodiment, as in the first embodiment, as shown in FIG. 6, in the sizing process, the punches 21 and 22 and the die 20 are compressed from both sides in the axial direction and the outer diameter side of the sintered body 1 ″. By shaping the inner diameter side of the sintered body 1 ″ with the core 23, it is possible to effectively utilize the expansion caused by sintering of the aluminum bronze sintered bearing and form the desired pores together with the dimension shaping of the sintered bearing 1. it can. Further, by adjusting the dimensional difference between the inner diameter dimension of the die 20 and the outer diameter dimension of the sintered body 1 ″ and the dimensional difference between the outer diameter dimension of the core 23 and the inner diameter dimension of the sintered body 1 ″, The size of the pores on the surface of the bonded body 1 ″ can be set. Thereby, the size of the pores on the surface of the sintered bearing 1 can be easily controlled.

  Also in the manufacturing method of the second embodiment described above, it is possible to realize a manufacturing method of a sintered bearing that is good in productivity, low in cost, and suitable for mass production. In addition, the sintered bearing based on the manufacturing method of the present embodiment can improve mechanical properties such as corrosion resistance and strength, wear resistance, oil film formation, and oil retention.

  A manufacturing method according to the third embodiment of the present invention will be described. The sintered bearing based on the manufacturing method of the present embodiment is specialized for a fuel pump of an automobile engine, suppresses sulfidation corrosion and organic acid corrosion due to poor gasoline, and has performance such as initial familiarity and durability. Excellent.

An example of a fuel pump for an automobile engine incorporating a sintered bearing based on the manufacturing method of the third embodiment is shown in FIG. In the fuel pump 40, the sintered bearing 1 is provided on the rotation side. Specifically, a casing 41 having a liquid inlet 41 a and a liquid outlet 41 b, a fixed shaft 2 fixed to the casing 41 and protruding into the internal space of the casing 41, and an impeller provided rotatably with respect to the fixed shaft 2 42, a motor 43, a magnet 44 attached to the impeller 42, and a magnet 45 attached to the rotating shaft of the motor 43 and facing the magnet 44 on the impeller 42 side in the radial direction. The sintered bearing 1 is fixed to the inner peripheral surface of the impeller 42, and the inner peripheral surface (bearing surface 1a, see FIG. 1) of the sintered bearing 1 and the outer peripheral surface of the fixed shaft 2 are slidably fitted in the rotation direction. Match. When the motor 43 is driven to rotate, the impeller 42 rotates due to the attractive force between the magnet 45 on the motor 43 side and the magnet 44 on the impeller 42 side. Thereby, the fuel which flowed into the internal space of the casing 41 from the liquid inlet 41a is sent out from the liquid outlet 41b .

Various studies and test evaluations are performed in order to suppress sulfidation corrosion and organic acid corrosion due to poor gasoline and to ensure performance such as initial familiarity and durability in an environment where the gasoline 34 is always in contact with the above. The present embodiment has been achieved with the following knowledge.
(1) Regarding the relationship between the amount of aluminum blended and the corrosion resistance, when the amount of aluminum increases, the diffusion to copper increases and the corrosion resistance effect is large.
(2) Regarding the relationship between the sintering temperature and the corrosion resistance, when the sintering temperature is increased, the diffusion of aluminum is enhanced and the corrosion resistance effect is large.
(3) With respect to the relationship between the density of the sintered bearing and the corrosion resistance, if the density is increased, the corrosion resistance effect is slightly improved.
(4) Additives (phosphorus, zinc, silicon) promote the diffusion of aluminum during the sintering process, which can reduce the amount of aluminum and reduce the corrosion resistance and initial familiarity. Can be reduced.

  As a sintered bearing for a fuel pump, in order to suppress sulfide corrosion and organic acid corrosion and improve performance such as initial familiarity and durability, in this embodiment, the aluminum content is 8 to 9% by mass, phosphorus Is 0.05 to 0.5 mass%, silicon is 0.5 to 3 mass%, zinc is 2 to 4 mass%, and the remaining main component is copper, copper powder, aluminum-copper alloy Powder, phosphorus alloy powder, silicon powder and zinc alloy powder are mixed, and 0.05 to 0.2% by mass of aluminum fluoride and calcium fluoride and 1 to 5% of graphite are added to the total of 100% by mass. Mix by mass to make raw material powder. The raw material powder has the same parts as those in the first and second embodiments described above, but details of each powder will be described below.

[Copper powder]
Copper powder includes atomized powder, electrolytic powder, and pulverized powder. Dendritic electrolytic powder is effective for sufficiently diffusing aluminum in copper, and is excellent in moldability, sinterability, and sliding characteristics. Therefore, in this embodiment, electrolytic powder was used as copper powder. The particle size is 100 mesh passing powder and 350 mesh passing powder ratio is 40% or less.

[Aluminum-copper alloy powder]
50 mass% aluminum-copper alloy powder was pulverized and the particle size was adjusted. The preferable particle size of the aluminum copper alloy powder is 145 mesh passing powder and the ratio of 350 mesh passing powder is 60% or more. By using the aluminum-copper alloy powder, the effects of additives such as graphite, phosphorus, and zinc are drawn, and the sintered bearing material is excellent in corrosion resistance, strength, sliding characteristics, and the like. Moreover, since it is alloyed, there is no problem in handling due to the scattering of the single powder of aluminum having a small specific gravity.

  As for the aluminum structure, the α phase is most excellent in sulfidation corrosion, corrosion resistance against organic acid corrosion, and initial familiarity. By using 50 mass% aluminum-copper alloy powder, strength can be obtained even when graphite is added, and a sintered bearing can be manufactured. When the structure is in the γ phase, the wear resistance is excellent, but the corrosion resistance and initial familiarity deteriorate.

  And in order to promote sintering of copper and aluminum, phosphorus alloy powder, zinc alloy powder, and fluoride (aluminum fluoride, calcium fluoride) are added. Thereby, diffusion of aluminum to copper is enhanced in liquid phase sintering and solid phase sintering. As the diffusion of aluminum increases, the corrosion resistance improves.

[Phosphor alloy powder]
As the phosphorus alloy powder, 8% by mass phosphorus-copper alloy powder was used as in the first and second embodiments. Phosphorus has the effect of increasing the wettability between the solid and liquid phases during sintering and shifting the liquid phase generation temperature generated by the addition of silicon powder to the low temperature side. The compounding amount of phosphorus is preferably 0.05 to 0.5% by mass. If the amount is less than 0.05% by mass, the effect of promoting the sintering between the solid and liquid phases is poor. On the other hand, if the amount exceeds 0.5% by mass, the sintering proceeds too much, so that the aluminum is segregated and the γ phase is precipitated, resulting in a sintered body. It becomes brittle.

[Zinc alloy powder]
Zinc-copper alloy powder was used as the zinc alloy powder. Zinc has a low melting point, promotes the sintering of copper and aluminum, and promotes the diffusion of aluminum. Furthermore, it is excellent in corrosion resistance.
As for the compounding quantity of zinc, 1 mass%-5 mass% are preferable. If it is less than 1% by mass, the effect of promoting the sintering of copper and aluminum and the effect of promoting the diffusion of aluminum cannot be obtained. On the other hand, if it exceeds 5% by mass, zinc evaporates during sintering and the sintering furnace is fouled, and sintering progresses too much, so that aluminum is segregated and diffusion of aluminum is inhibited.

[Silicon powder]
Silicon is added as a sintering aid. Silicon generates a copper silicon-based liquid phase for the sintering progress-inhibiting phase formed in the sintering process and promotes the sintering. Since silicon increases the diffusion of aluminum during the sintering process, the amount of aluminum can be reduced and the γ phase can be reduced. The blending amount of silicon is preferably 0.5 to 3% by mass. If it is less than 0.5% by mass, the effect of enhancing the diffusion of aluminum in the sintering process is insufficient, and accordingly, the effect of reducing the γ phase becomes insufficient. On the other hand, if it exceeds 3% by mass, silicon reacts when the temperature rises during sintering, and aluminum is oxidized black, resulting in a discoloration defect.

[Graphite powder]
Graphite exists mainly as free graphite in pores dispersed and distributed in the base material, imparts excellent lubricity to the sintered bearing, and contributes to improvement of wear resistance. As for the compounding quantity of graphite, 1-5 mass% is preferable with respect to a total of 100 mass% of aluminum, silicon, tin, phosphorus, copper, and an unavoidable impurity. If it is less than 1% by mass, the effect of improving the lubricity and wear resistance by adding graphite cannot be obtained. On the other hand, if it exceeds 5% by mass, the strength decreases, which is not preferable.

[Aluminum fluoride and calcium fluoride]
Since aluminum fluoride and calcium fluoride are the same as those in the second embodiment described above, duplicate description is omitted.

  Since the metal structure of the cross section of the sintered bearing based on the manufacturing method of the present embodiment is also the same as that of the first and second embodiments shown in the schematic diagram of FIG. The duplicate description is omitted for the portion. As shown in FIGS. 2 (a), 2 (b), and 2 (c), the sintered bearing 1 of the present embodiment is an aluminum-copper alloy structure with hatched 3 and aluminum oxide around the surface and internal pores. Film 4 is present. For this reason, it is excellent in corrosion resistance and abrasion resistance. Although illustration is omitted, phosphorus exists in the grain boundary portion of the aluminum-copper alloy structure 3. Since the free graphite 5 is distributed in the pores, it is excellent in lubricity and wear resistance.

  Also in the sintered bearing 1 based on the manufacturing method of the present embodiment, as shown in FIG. 7, both the outer diameter surface 1b and the inner bearing surface 1a of the bearing are sized after sintering. And since an aluminum copper series sintered bearing expand | swells by sintering, the outer-diameter surface 1b of a bearing is sized in a bigger quantity than the bearing surface 1a of an internal diameter side. Therefore, the pores do (see FIG. 2C) of the surface layer portion on the outer diameter surface 1b side are crushed more than the pores db (see FIG. 2A) of the surface layer portion on the bearing surface 1a side. Comparing the sizes of the pores do in the surface layer portion on the outer diameter surface 1b side, the pores db in the surface layer portion on the bearing surface 1a side, and the pores di (see FIG. 2B) inside the bearing that are not crushed, do <db <di It becomes a relationship. Because of this relationship, the bearing surface 1a side can improve the corrosion resistance and oil film formation, while the outer surface 1b side and the end surface 1c side close to the sealed state have corrosion resistance and oil retention. Can be improved. Lubricating oil is impregnated in the pores do, db, and di of the sintered bearing 1. Thereby, a better lubrication state can be obtained than at the start of operation. As the lubricating oil, mineral oil, polyalphaolefin (PAO), ester, liquid grease, and the like can be used. However, it is not always necessary to impregnate the lubricating oil for the intended use of the bearing.

  Furthermore, the state of the compression layer of the surface layer of the sintered bearing 1 based on the manufacturing method of this embodiment is the same as that of the sintered bearing based on the manufacturing method of the first and second embodiments shown in FIG. That is, also in the sintered bearing 1 based on the manufacturing method of this embodiment, as shown in FIG. 1, the surface layer of the sintered bearing 1 has a compression layer with hatching. Expressed by the above-described equation of density ratio α, the density ratio αo of the surface compression layer Po on the outer diameter surface 1b side and the density ratio αb of the surface compression layer Pb on the bearing surface 1a side are both internal density ratio αi. The density ratios αo and αb are both set in the ranges of 80% ≦ αo and αb ≦ 95%.

  The average value of the depth of the compression layer Po of the surface layer on the outer diameter surface 1b side is To, the average value of the depth of the compression layer Pb of the surface layer on the bearing surface 1a side is Tb, and the inner diameter dimension D1 of the bearing surface If the ratios are To / D1 and Tb / D1, respectively, they are set to 1/100 ≦ To / D1 and Tb / D1 ≦ 1/15.

  Since the manufacturing method of the third embodiment is also the same as the manufacturing method of the first and second embodiments shown in FIG. 3, the specific steps in the raw material powder preparation step S1, the sintering step S3, and the sizing step S4 are described. Only the differences will be described.

[Raw material powder preparation step S1]
The raw material powders are electrolytic copper powder remaining mass%, 40-60 mass% aluminum-copper alloy powder 14-20 mass%, 8 mass% phosphorus-copper alloy powder 2-4 mass%, silicon powder 1 3 to 20% by mass and a total of 100 to 10% by mass of zinc to copper alloy powder of 6 to 8% by mass, and 0.05 to a total of aluminum fluoride and calcium fluoride as a sintering aid. 0.2% by mass, 1 to 5% by mass of graphite powder, and 0.5% by mass of a lubricant such as zinc stearate and calcium stearate were added to facilitate moldability.

[Sintering step S3]
What is important in the sintering process is to improve the corrosion resistance and bearing performance (initial familiarity) by sufficiently diffusing aluminum into copper and improving the corrosion resistance, and by making the aluminum structure alpha phase. is there. When it becomes the γ phase, it becomes hard and has excellent wear resistance, but the corrosion resistance decreases. Therefore, it has been found that it is necessary to reduce the amount of aluminum so as to suppress the precipitation of the γ phase as much as possible.

  As a sintering condition that satisfies the above, the sintering temperature is preferably 900 to 950 ° C, and more preferably 900 to 920 ° C (for example, 920 ° C) as a sintered bearing for a fuel pump. The atmosphere gas may be hydrogen gas, nitrogen gas or a mixed gas thereof, and the sintering time may be longer for better corrosion resistance. For a sintered bearing for a fuel pump, 20 to 60 minutes (for example, 30 minutes) Is preferred.

[Sizing process S4]
Also in the sintered bearing of the present embodiment, as in the first and second embodiments, as shown in FIG. 6, both sides of the sintered body 1 ″ in the axial direction and the outer side by the punches 21 and 22 and the die 20 in the sizing process. By compressing from the radial side, the inner diameter side of the sintered body 1 ″ is shaped by the core 23, so that the expansion due to the sintering of the aluminum bronze sintered bearing can be effectively utilized, and the desired size of the sintered bearing 1 can be shaped. Pores can be formed. Further, by adjusting the dimensional difference between the inner diameter dimension of the die 20 and the outer diameter dimension of the sintered body 1 ″ and the dimensional difference between the outer diameter dimension of the core 23 and the inner diameter dimension of the sintered body 1 ″, It is possible to set the size of the pores on the surface of the bonded body 1 ″. Thereby, the size of the pores on the surface of the sintered bearing 1 can be easily controlled. By rotating and sizing the surface 1a (see FIG. 7), the pores of the bearing surface 1a can be reduced.

  Also in the manufacturing method of the third embodiment, it is possible to realize a method for manufacturing a sintered bearing that is good in productivity, low in cost, and suitable for mass production. In addition, in the sintered bearing based on the manufacturing method of the present embodiment, it is possible to improve mechanical properties such as corrosion resistance, strength, wear resistance, oil film formation, oil retention, and to achieve compactness and cost reduction. it can. In particular, as a sintered bearing for a fuel pump, it suppresses sulfidation corrosion and organic acid corrosion due to poor gasoline, and is excellent in performance such as initial familiarity and durability.

  Although the fuel pump is illustrated as an application of the sintered bearing based on the manufacturing method of the above embodiment, the present invention is not limited to this. For example, corrosion resistance such as an exhaust gas recirculation device (EGR) or a fishing reel is required. The method can be appropriately applied to a method for manufacturing a sintered bearing for a particular application.

  In the above description, the case where the sintered bearing based on the manufacturing method of each embodiment is applied to a perfect circle bearing with the bearing surface 1a having a perfect circle shape is exemplified. However, the sintering based on the production method of the present invention is exemplified. The bearing is not limited to a perfect circle bearing, and can be similarly applied to a fluid dynamic pressure bearing in which a dynamic pressure generating portion such as a herringbone groove or a spiral groove is provided on the outer peripheral surface of the bearing surface 1a or the shaft 2.

  The present invention is not limited to the above-described embodiments, and can of course be implemented in various forms without departing from the scope of the present invention. The scope of the present invention is not limited to patents. It includes the equivalent meanings recited in the claims and the equivalents recited in the claims, and all modifications within the scope.

DESCRIPTION OF SYMBOLS 1 Sintered bearing 1 'Compact 1 "Sintered body 1a Bearing surface 1b Outer diameter surface 1c End surface 2 Shaft 3 Aluminum copper alloy structure 4 Aluminum oxide film 5 Free graphite 15 Mesh belt type continuous furnace 20 Die 21 Upper punch 22 Lower Punch 23 Core 40 Fuel pump D1 Bearing surface inner diameter db Pore di Pore do Pore Ti Compressed layer To Compressed layer

Claims (1)

  A method of manufacturing a sintered bearing containing 3 to 12% by mass of aluminum and 0.05 to 0.5% by mass of phosphorus, the remaining main component being copper and containing inevitable impurities, A compacting step of forming a green compact in which a sintering aid is added to the raw material powder, and a sintering step of obtaining a sintered body having a structure in which an aluminum-copper alloy is sintered from the green compact And a sizing step for sizing the sintered body, wherein the mold of the sizing step is composed of a die, a pair of punches and a core, and both sides of the sintered body in the axial direction and outside are formed by the punch and the die. By compressing from the diameter side, the inner diameter side of the sintered body is shaped by the core, the dimensional difference between the inner diameter dimension of the die and the outer diameter dimension of the sintered body, and the outer diameter dimension of the core and the sintering Adjust the dimensional difference with the inner diameter of the body And a method for producing a sintered bearing, characterized in that setting the size of the pores of the surface of the sintered body.

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