SINTERED SLIDING MATERIAL EXHIBITING EXCELLENT CORROSION RESISTANCE, HEAT RESISTANCE, AND WEAR RESISTANCE, AND PRODUCTION METHOD THEREFOR

Abstract

This sintered sliding material has a composition including, by mass %, 10% to 35% of Ni, 5% to 12% of Sn, 0% to 0.9% of P, and 4.1% to 9% of C, with a remainder of Cu and inevitable impurities, wherein the sintered sliding material includes a sintered body of a plurality of CuNi alloy grains containing Sn and C, the sintered sliding material has a structure in which pores are dispersedly formed in grain boundaries of the plurality of alloy grains and free graphite is distributed in the pores, and an amount of C in a metal matrix including the alloy grains is, by mass %, 0% to 0.07%.

Claims

1. A sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance, comprising, by mass %: 10% to 35% of Ni; 5% to 12% of Sn; 0% to 0.9% of P; 4.1% to 9% of C; and a remainder of Cu and inevitable impurities, wherein the sintered sliding material includes a sintered body of a plurality of CuNi alloy grains containing Sn and C, the sintered sliding material has a structure in which pores are dispersedly formed in grain boundaries of the plurality of alloy grains and free graphite is distributed in the pores, and an amount of C in a metal matrix including the alloy grains is, by mass %, 0% to 0.07%.

2. The sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance according to claim 1, wherein a porosity of the sintered body is 8% to 21%.

3. The sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance according to claim 1, wherein a Sn-rich alloy layer is formed in at least a part of an outer circumferential portion of the sintered body and in at least a part of the pores of the sintered body.

4. A method for producing a sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance, which is a method for producing the sintered sliding material according to claim 1, the method comprising the steps of: conducting deoxidation by any one of phosphorus, zinc, or manganese to prepare a CuNi alloy powder in which an amount of C is in a range of 0 to 0.07 mass %; mixing the CuNi alloy powder, a Sn powder, and a CuP alloy powder so as to have a total composition including, by mass %, 10% to 35% of Ni, 5% to 12% of Sn, 0% to 0.9% of P, and 0% to 0.07% of C, with a remainder of Cu and inevitable impurities, thereby obtaining a raw material powder; mixing the raw material powder with a graphite powder to obtain a mixed raw material powder, and press-molding and sintering the mixed raw material powder to obtain a sintered body; and sizing the sintered body.

5. The method for producing a sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance according to claim 4, wherein the graphite powder is mixed with the raw material powder so that a total sum of C contained in the raw material powder and C contained in the graphite powder becomes 4.1% to 9% in the mixed raw material powder.

6. (canceled)

7. The method for producing a sintered sliding material exhibiting excellent corrosion resistance, heat resistance, and wear resistance according to claim 4, wherein a porosity of the sintered body is made to be 8% to 21%.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0025] FIG. 1 is a perspective view showing an example of a ring-shaped bearing member formed of a sintered sliding material according to the present invention.

[0026] FIG. 2 is an enlarged structural diagram of the sintered sliding material constituting the bearing member.

[0027] FIG. 3 is an exploded side view showing an example of a fuel pump provided with the bearing member.

DETAILED DESCRIPTION OF THE INVENTION

[0028] Hereinafter, one embodiment of the present invention will be described with reference to the drawings.

[0029] In the drawings used in the following description, for the purpose of emphasizing a characteristic portion, there are cases where a portion that is characteristic portion is enlarged for convenience and a dimensional ratio or the like of each constituent element is not necessarily the same as an actual one. In addition, for the same purpose, some portions that are not characteristic may be omitted for illustration.

[0030] FIG. 1 shows a tubular bearing member 1 consisting of a sintered sliding material according to the present embodiment. As an example, the bearing member 1 is composed of a sintered sliding material having a sectional structure shown in FIG. 2, and is applied as a bearing member 1 in a motor-type fuel pump 2 shown in FIG. 3.

[0031] In the motor-type fuel pump 2 shown in FIG. 3, a motor (armature) 5 is provided inside a cylindrical casing 3 and surrounded by magnets 4, and both ends of a rotating shaft 6 of the motor 5 are rotatably supported by bearing members 1 which are provided, respectively, inside the casing 3.

[0032] In a configuration of FIG. 3, an impeller 7 is provided on one end side of the rotating shaft 6, and a narrow gasoline flow path is formed along an outer circumferential surface of the impeller 7, an outer circumferential surface of the motor 5, and a gap between the bearing members 1, 1 and the rotating shaft 6.

[0033] The motor-type fuel pump 2 rotates the impeller 7 by rotation of the motor 5, and gasoline is taken into the casing 3 from an intake port 8 provided on one end side of the casing 3 by a rotational force of the impeller 7 and the gasoline can flow along the above-described gasoline flow path. The gasoline can be delivered from a delivery port 9 provided on the other end side of the casing 3.

[0034] As an example, the motor-type fuel pump 2 is provided so as to be immersed in gasoline in a fuel tank of an internal combustion engine, and the delivery port 9 of the fuel pump 2 is connected to a fuel injection portion of the engine via a filter device and an injector which are not shown.

[0035] The motor-type fuel pump 2 shown in FIG. 3 is always used in a state of being immersed in gasoline and the bearing member 1 supporting the rotating shaft 6 is also used in a state of being always immersed in gasoline. Thus, excellent corrosion resistance against gasoline is desired for the bearing member 1.

[0036] Therefore, as shown in the sectional structural diagram of FIG. 2, the bearing member 1 of the present embodiment consists of the sintered sliding material 10 having a structural configuration in which pores 12 (internal pores 12a and open pores 12b) are dispersed in grain boundary portions of a plurality of alloy grains 11, and free graphite (C (Free)) 13 is dispersed inside the pores 12. The alloy grains 11 include (consist of) CuNi alloy grains containing Sn, P, and C, and the plurality of alloy grains 11 are sintered to constitute a metal matrix, and the pores 12 dispersed around the alloy grains 11 and the free graphite 13 are further present to constitute the entire structure of the sintered sliding material 10.

[0037] A Sn-rich alloy layer 14 is formed on an inner surface of the internal pore 12a present in the sintered sliding material 10, on an inner surface of the open pore 12b formed to be open to a surface of the sintered sliding material 10, and at or in the vicinity of an opening of the open pore 12b. The Sn-rich alloy layer 14 contains 30 mass % or more of Sn, and has an effect of enhancing corrosion resistance of the sintered sliding material 10 against organic acids.

[0038] As shown in FIG. 2, the Sn-rich alloy layer 14 is not formed at a portion where a generation interval of the open pores 12b is wide in an outer circumferential portion of the sintered sliding material 10, and an exposed portion 15 where the alloy grains 11 are exposed may be formed. However, since the exposed portion 15 is not the open pore 12b, it hardly affects corrosion resistance against organic acids. As shown in FIG. 2, it is preferable that the Sn-rich alloy layer 14 is formed substantially over the entire outer circumferential portion of the sintered sliding material 10, and it is preferable that the Sn-rich alloy layer 14 is formed so as to close the open pores 12b on an outer surface of the sintered sliding material 10.

[0039] A method for producing the sintered sliding material 10 will be described in detail later. However, as an example thereof, the sintered sliding material 10 is obtained by a method which includes: uniformly mixing predetermined amounts of a CuNi alloy powder, a Sn powder, a CuP powder, and a graphite powder to obtain a raw material powder; press-molding the raw material powder; and sintering the obtained molded body at a temperature of 860 C. to 970 C.

[0040] Excellent sliding characteristics and corrosion resistance are ensured for the bearing member 1 due to the alloy grains 11 including (consisting of) CuNi alloy grains that constitute the metal matrix. High lubricating performance is obtained due to a lubricating action of the free graphite having high lubricity and distributed in the pores 12 dispersedly distributed in the entire structure of the bearing member 1. Furthermore, wear resistance is further improved due to an action of a fluid lubricating film formed by a liquid fuel supplied from an outer circumferential surface of the bearing member 1 to an inner circumferential surface of the bearing member 1 through the pores 12 existing inside the bearing member 1.

[0041] A composition ratio of the sintered sliding material 10 is preferably, by mass %, 10% to 35% of Ni, 5% to 12% of Sn, 0% to 0.9% of P, and 4.1% to 9% of C. In addition, the amount of C as an inevitable impurity contained in the metal matrix including (consisting of) the CuNi alloy grains 11 is preferably, by mass %, in a range of 0% to 0.07%. In the present specification, in the case where the range of the amount of an element is indicated, unless otherwise specified, the range includes an upper limit and a lower limit. Therefore, 10% to 35% of Ni means a range of 10% or more and 35% or less.

[0042] The reasons for limiting the respective composition ratios will be described below.

[0043] Ni: 10% to 35%

[0044] Ni has an effect of imparting excellent strength, wear resistance, heat resistance, and corrosion resistance to the sintered sliding material 10. In the case where an amount of Ni is less than 10%, wear resistance, heat resistance, and corrosion resistance become insufficient to meet the desired properties for the sintered sliding material 10, and in the case where the amount of Ni exceeds 35%, material cost for the sintered sliding material is high, which is not preferable.

[0045] The amount of Ni is preferably 16% to 33%, and more preferably 20 to 28%.

[0046] Sn: 5% to 12%

[0047] Sn together with Cu, Ni, and P form a solid solution in the alloy grains 11, and thereby, Sn has an effect of improving strength and wear resistance of the sintered sliding material 10. Sn causes the Sn-rich alloy layers 14 to be formed on inner surfaces of the internal pores 12a and the open pores 12b, and peripheries of openings of the open pores 12b in the sintered sliding material 10. The Sn-rich alloy layer 14 is also formed on an outer circumferential portion of the sintered material 10. The Sn-rich alloy layer 14 has an effect of improving corrosion resistance of the sintered sliding material 10. In the case where an amount of Sn is less than 5%, desired corrosion resistance and wear resistance are not obtained, and in the case where the amount of Sn is 12% or more, a large amount of liquid phases is generated during sintering and a dimension of the sintered material varies, which is not preferable.

[0048] The amount of Sn is preferably 6% to 11%, and more preferably 7 to 10%.

[0049] P: 0% to 0.9%

[0050] P has an effect of improving sinterability and improving strength of a matrix with respect to the sintered sliding material 10 of the present embodiment. However, in the case where an amount of P exceeds 0.9%, deformation of a sintered body occurs and a product yield decreases, which is not preferable.

[0051] The amount of P is preferably 0.2% to 0.8%, and more preferably 0.3% to 0.6%.

[0052] C: 4.1% to 9%

[0053] C mainly exists as free graphite in pores dispersedly distributed in a matrix of the sintered sliding material 10, C imparts excellent lubricity to the sintered sliding material 10, and C improves wear resistance. In the case where an amount of C is less than 4.1%, sufficient lubricating effect is not obtained and a function as a bearing material cannot be exhibited. In the case where the amount of C is 9% or more, dimensional instability occurs during sintering, which is not preferable.

[0054] The amount of C is preferably 4.2 to 8.8%, and more preferably 4.4 to 6.7%.

[0055] Amount of C in CuNi alloy powder: 0% to 0.07%

[0056] In the case where an amount of impurity carbon in the CuNi alloy powder is more than 0.07%, a rate of dimensional change becomes high during sintering and a dimension is unstable, which is not preferable. The amount of C in the CuNi alloy powder is preferably in a range of 0.001% to 0.07%. The impurity carbon amount of 0.001% is an amount which is introduced as a inevitable impurity due to carbon deoxidation or the like. The amount of impurity carbon in the CuNi alloy powder corresponds to an amount of C in a metal matrix including (consisting of) CuNi alloy grains obtained after sintering.

[0057] The deoxidation can be conduced by not only carbon but also phosphorus, zinc, manganese, or the like. However, there is a possibility of being incorporated as an impurity from a graphite crucible used in the case of producing powders with an atomizing method, and carbon is an element which is incorporated as an inevitable impurity. However, it is also possible to prevent incorporation of carbon by replacing the graphite crucible with an alumina crucible or the like. Therefore, the amount of C in the CuNi alloy powder may be 0%.

[0058] The amount of C in the CuNi alloy powder is preferably 0.003% to 0.068%, and more preferably 0.016% to 0.059%.

[0059] Porosity: 8 to 21%

[0060] Pores dispersedly distributed in a base (matrix) of a sintered material have an action of alleviating a strong friction and a high surface pressure which the bearing receives under high-pressure and high-speed circulation of liquid fuel, for example, in the case where a bearing consisting of the sintered sliding material 10 of the present embodiment is used in a fuel pump. Thereby, the pores remarkably suppress wear of the bearing. However, in the case where a porosity of the sintered sliding material 15 is less than 8%, a proportion of pores distributed in the base is small and the above-described effect of action is not sufficiently obtained, whereas in the case where the porosity of the sintered sliding material 10 is more than 21%, wear resistance decreases, which is not preferable.

[0061] The porosity is preferably 8.1% to 18.2%, and more preferably 11.2% to 16.6%. The percentage of the porosity is vol %.

[0062] Production Method of Sintered Sliding Material

[0063] In order to produce the sintered sliding material 10 of the present embodiment, a CuNi alloy powder, a Sn powder, a CuP powder, and a graphite powder are prepared as starting materials. Each of these powders preferably has a predetermined average particle diameter in a range of about 10 to 100 m.

[0064] These powders are mixed so as to achieve a final target composition ratio, and then a lubricant such as zinc stearate is added at an amount of 0.1% to 1.0%, for example, about 0.5% and the mixture is mixed uniformly by a V type mixer for about several tens of minutes to obtain a mixed raw material powder. Next, the mixed raw material powder is charged into a mold of a press machine, and the mixed raw material powder is press-molded to obtain a target shape, for example, a ring-shaped green compact.

[0065] The green compact is sintered at a predetermined temperature in a range of 860 C. to 970 C. in, for example, an endothermic gas atmosphere, and the endothermic gas atmosphere is obtained by a method which includes: mixing natural gas and air; and passing the mixture through a heated catalyst to decompose and convert the mixture. Thereby, it is possible to obtain a targeted ring-shaped sintered sliding material.

[0066] Sn (about 232 C.) and CuP (about 714 C.), which are low melting-point raw materials, melt during the sintering procedure, Sn and P diffuse into grains (particles) including (consisting of) a CuNi alloy (powder) and are alloyed therewith. Therefore, after sintering, the sintered sliding material 10 having the structure shown in FIG. 2 is obtained, and in the structure, the free graphite 13 exists in pore portions of grain boundaries of the CuNi alloy grains in which Sn and P are solid-solubilized.

[0067] Further, when Sn and P diffuse into grains (particles) including (consisting of) a CuNi alloy (powder) to form CuNi alloy grains in which Sn and P are solid-solubilized, the Sn-rich alloy layer is formed.

[0068] When producing the CuNi alloy powder, an atomizing method is used, in which a molten alloy is rapidly cooled to perform pulverization. C contained in the alloy powder can be reduced by controlling an addition amount of C used for deoxidation, a material of a crucible, time to melt the alloy, a melting temperature of the alloy, and the like.

[0069] The sintered sliding material 10 produced as described above is a sintered material obtained by sintering CuNi alloy grains, and it is obtained as a sintered sliding material in which free carbon is dispersed in pores of grain boundaries of CuNi alloy grains. Thus, it is possible to provide a sintered sliding material which is excellent in wear resistance and lubricity and which is excellent in corrosion resistance under high-temperature corrosive environment required for a sliding material to be used under high-temperature corrosive environments.

[0070] Further, by setting an amount of C as an impurity contained in grains of the CuNi alloy to be in a range of 0.001% to 0.07%, it is possible to provide the sintered sliding material 10 which is hard to cause a large dimensional change such as abnormal expansion or shrinkage before and after sintering, and can be produced with good yield.

[0071] Further, the sintered sliding material 10 of the present embodiment is suitable as a bearing member, a bush for EGR, or the like which is always immersed in gasoline such as a motor-type fuel pump, and it can provide a sintered sliding material which is excellent in corrosion resistance and wear resistance even in the case of being immersed in mixed gasoline, which contains corrosive liquid such as light oil, alcohol, or other organic acids in gasoline, depending on regions.

[0072] Furthermore, the sintered sliding material 10 is also suitable for a bearing member used in a recirculation exhaust gas flow-rate adjustment valve, and it is possible to provide a sintered sliding material which is excellent in wear resistance and corrosion resistance even under a severe environment exposed to high-temperature exhaust gas.

EXAMPLES

[0073] Hereinafter, the present invention will be described in more detail with reference to examples, but the present invention is not limited to these examples.

Example 1

[0074] As raw material powders, a CuNi powder with a particle diameter of 100 mesh, a Sn atomized powder with a particle diameter of 250 mesh, a Cu-8% P atomized powder with a particle diameter of 200 mesh, and a graphite powder with a particle diameter of 150 mesh were prepared. The atomized powders are powders obtained by a method which included: forming a molten alloy having a target composition in a crucible in a high-frequency melting furnace; and spraying this molten alloy into water from an injection nozzle at a bottom of the crucible and rapidly cooling the molten alloy to be pulverized. In the atomizing method used in the examples, an atomizing device is used in which an inverted conical jet water stream was injected from an injection flow path provided inside a molten metal blowout part of an injection nozzle and the molten metal was sprayed toward the inverted conical jet water stream to be pulverized.

[0075] These raw material powders were blended in blending proportions as shown in Table 1 so as to obtain a final component composition as shown in Table 2 below, and 0.5% of zinc stearate was added. The mixture was mixed by a V type mixer for 20 minutes, and then the mixture was press-molded to produce a green compact. Next, this green compact was sintered at a predetermined temperature in a range of 860 C. to 970 C. shown in Table 1 in an endothermic gas atmosphere. The endothermic gas atmosphere was obtained by a method which included: mixing natural gas and air; and passing the mixture through a heated catalyst to decompose and convert the mixture. Then, sizing was performed at a predetermined pressure in a range of 200 to 700 MPa to obtain a sintered sliding material.

[0076] Each of the sintered sliding materials had a dimension of an outer diameter of 10 mman inner diameter of 5 mm x a height of 5 mm and was a ring-shaped sintered sliding material (bearing member) consisting of a CuNiSn-based sintered alloy having a component composition shown in Table 2 below. Examples of sample Nos. 1 to 15, and ring-shaped test pieces of sample Nos. 1 to 7 having the same shape as comparative examples were produced and the following tests were conducted.

[0077] In the raw material powders, an amount of C as an impurity element contained in the CuNi powder was controlled by adjusting an amount of impurities contained in the raw materials before an atomizing treatment for producing the CuNi powder.

[0078] Specifically, samples of Examples Nos. 1 to 15 were prepared by blending the raw materials having impurity amounts (C amounts) shown in Table 1 so as to have compositions shown in Table 1 and Table 2. In addition, samples of Comparative Examples Nos. 1 to 7 were prepared by using and blending raw materials having impurity C amounts shown in Table 1 as so as to have compositions shown in Table 1 and Table 2.

[0079] The porosity, the radial crushing strength, the rate of dimensional change, the product yield, the corrosion resistance, and the wear resistance were tested using the samples of Examples Nos. 1 to 15 and the samples of Comparative Examples Nos. 1 to 7. The results are shown all together in Table 2.

[0080] In the component composition shown in Table 2, the C (Free) column represents mass % of C intervening at grain boundaries as free graphite. In addition, the C (Combined) column represents mass % of C alloyed with and contained in the alloy grains. Furthermore, the C (Total: total amount) represents a total amount, by mass %, of C contained in the sample as C (Free) and C (Combined).

[0081] Details for measurement methods of the rate of dimensional change, the determination criteria of product yield, the corrosion resistance test evaluating the corrosion resistance, and the wear resistance test evaluating the wear resistance which are shown in Table 2 are as follows. [0082] Rate of dimensional change (DC): An outer diameter dimension of a molded body (green compact) after press molding was measured in advance before sintering and sintering was carried out. The outer diameter dimension of the sintered body (sintered sliding material) after sintering was measured, and a rate of dimensional change before and after sintering was calculated and obtained. [0083] Yield: A ratio of samples of which an inner diameter dimension of a sized body after sizing was within a dimensional tolerance (0.006 mm) was taken as a yield. From measurement results of 50 samples, the case where 96% or more of the samples were acceptable (within the dimensional tolerance (0.006 mm)) was determined as A, the case where 90% or more and less than 96% of the samples were acceptable was determined as B, and the case where less than 90% of the samples were acceptable was determined as C. [0084] Corrosion resistance test: Supposing pseudo bad gasoline, an organic acid test liquid which was produced by adding carboxylic acid represented by RCOOH (R is a hydrogen atom or a hydrocarbon group) to gasoline.

[0085] A corrosion resistance test was conducted by immersing a plurality of sample bearing members 1 in this organic acid test liquid for 200 hours in a hot bath (60 C.).

[0086] After the corrosion resistance test, products attached to a surface of the bearing member 1 were removed with chemicals, a rate of change of mass was measured from a mass of the bearing member 1 before immersion in the organic acid test liquid and a mass of the bearing member 1 after removing the attached products after immersion. In the column of corrosion resistance of each table, a sample with 0(rate of change of mass)0.50% was indicated by A, and a sample with 0.50%>(rate of change of mass) was indicated by C.

[0087] Wear resistance test of bearing for fuel pump: A wear resistance test was conducted under conditions where gasoline circulated in a narrow space at a high speed, and a bearing received a high pressure due to high-speed rotation of a motor causing such circulation and the bearing was exposed to gasoline of a high flow speed. The bearing member 1 was assembled into a fuel pump whose outer dimension was 110 mm40 mm in length, and the fuel pump was installed in a gasoline tank.

[0088] An actual machine test was conducted under conditions where an impeller rotation speed was 5,000 to 15,000 rpm, a gasoline flow rate was 50 to 250 liters/hour, a pressure that the bearing member 1 received from a high-speed rotation was a maximum of 500 kPa, and a test time was 500 hours. In a maximum wear depth on a bearing surface after the test, a sample with 0(maximum wear depth)10 m was indicated by A, and a sample with 10 m<(maximum wear depth) was indicated by C.

[0089] This result is described in the column of wear resistance (1). [0090] Wear resistance test of bearing for recirculation exhaust gas flow-rate adjustment valve: A shaft made of a stainless steel (JIS.Math.SUS 303) having a dimension of a diameter of 5a length of 60 mm and the bearing member 1 were assembled together into a recirculation exhaust gas flow-rate adjustment valve of an EGR type gasoline engine, and a wear test was conducted under conditions where an engine rotation speed was 3,000 rpm, a stainless steel shaft reciprocating distance was 10 mm, a stainless steel shaft reciprocating number was 150 times/minute, and a test time was 500 hours. After the wear test, the maximum wear depth of the bearing was measured.

[0091] The temperature of the bearing under test was in a range of 420 C. to 435 C.

[0092] In a maximum wear depth on a bearing surface after the test, a sample with 0(maximum wear depth)70 m was indicated by A, and a sample with 70 m<(maximum wear depth) was indicated by C. This result is described in the column of wear resistance (2).

[0093] A porosity was measured in accordance with the open porosity test method JPMA M 02-1992 of sintered metal material published by the Japan Powder Metallurgy Association.

[0094] <Carbon Analysis in Raw Material Powder and Sintered Body>

[0095] The amount of impurity carbon in the CuNi powder was measured by an infrared absorption method.

[0096] Further, in the total amount of C contained in each sample of sintered body, the ratio of C (free) intervening at grain boundaries as free graphite to C (Combined) alloyed with and contained in alloy grains was obtained by the following method.

[0097] First, the total amount of C contained in a sintered bearing of a sample was measured by infrared absorption method (gas analysis). Next, analysis of the amount of C (Free) contained as free carbon was carried out according to the method of JIS G1211-1995. The amount of C (Combined) alloyed with and contained in the alloy grains was obtained by subtracting the amount of the free graphite from the total amount of C.

TABLE-US-00001 TABLE 1 Blending composition (mass %) of raw material powders Graphite (C) Combined C (mass %) Sintering Bearing CuNi powder CuP powder Sn powder powder Total in CuNi powder temperature ( C.) Invention 1 Cu13% Ni: 78% Cu8% P: 4.0 9 9 100 0.010 870 Example 2 Cu15% Ni: 85.5% Cu8% P: 3.0 7 4.5 100 0.034 860 3 Cu20% Ni: 79.5% Cu8% P: 5.0 11 4.5 100 0.028 890 4 Cu20% Ni: 86% Cu8% P: 3.0 5 6 100 0.035 900 5 Cu25% Ni: 88% Cu8% P: 0 7 5 100 0.032 915 6 Cu25% Ni: 80.5% Cu8% P: 4.0 10 5.5 100 0.001 920 7 Cu30% Ni: 80% Cu8% P: 5.0 10 5 100 0.017 900 8 Cu30% Ni: 80% Cu8% P: 3.0 12 5 100 0.045 915 9 Cu30% Ni: 81.5% Cu8% P: 2.5 9 7 100 0.051 940 10 Cu30% Ni: 81% Cu8% P: 8.0 6 7 102 0.039 950 11 Cu30% Ni: 82.5% Cu8% P: 2.5 10 5 100 0.017 910 12 Cu35% Ni: 79% Cu8% P: 5.0 11 5 100 0.064 920 13 Cu35% Ni: 78.5% Cu8% P: 7.5 9 5 100 0.041 910 14 Cu40% Ni: 80.5% Cu8% P: 10 5 4.5 100 0.053 970 15 Cu40% Ni: 81% Cu8% P: 4.0 10 5 100 0.053 930 Comparative 1 Cu10% Ni: 85% Cu8% P: 3.0 8 4 100 0.006 850 Example 2 Cu20% Ni: 92% Cu8% P: 3.0 1 4 100 0.063 890 3 Cu30% Ni: 79% Cu8% P: 3.0 14 4 100 0.037 890 4 Cu40% Ni: 67% Cu8% P: 15 9 9 100 0.053 925 5 Cu30% Ni: 76% Cu8% P: 5.0 8 11 100 0.055 925 6 Cu40% Ni: 87.5% Cu8% P: 3.0 9 0.5 100 0.053 890 7 Cu40% Ni: 80% Cu8% P: 5.0 9 6 100 0.127 890

TABLE-US-00002 TABLE 2 Combined C Free C (mass %) (mass %) in in Component composition (mass %) sintered sintered Porosity Bearing Ni Sn P C (Total) Cu material material (%) Invention 1 10.1 8.8 0.3 8.8 Remainder 0.016 8.784 8.1 Example 2 12.7 6.9 0.2 4.4 Remainder 0.032 4.368 11.2 3 15.9 11 0.4 4.2 Remainder 0.030 4.17 13.5 4 17.2 5.1 0.2 6.0 Remainder 0.041 5.959 12.8 5 22.0 7.3 0 5.0 Remainder 0.050 4.95 13.1 6 20.1 9.9 0.3 5.3 Remainder 0.003 5.297 20.8 7 24.0 9.8 0.4 4.7 Remainder 0.022 4.678 15.3 8 24.0 11.7 0.5 5.1 Remainder 0.033 5.067 17.9 9 24.5 9.0 0.2 6.7 Remainder 0.066 6.634 16.6 10 24.3 5.9 0.6 6.7 Remainder 0.049 6.651 14.8 11 24.8 9.9 0.2 4.9 Remainder 0.021 4.879 12.6 12 27.7 10.8 0.4 5 Remainder 0.068 4.932 18.2 13 27.5 9.7 0.6 5 Remainder 0.046 4.954 16.6 14 32.3 5.2 0.8 4.3 Remainder 0.055 4.245 14.8 15 32.6 10.0 0.3 4.6 Remainder 0.059 4.541 15.5 Comparative 1 8.7 7.7 0.2 4 Remainder 0.005 3.995 7.5 Example 2 18.4 1.1 0.2 4.2 Remainder 0.054 4.146 12.8 3 23.7 14.3 0.2 4.2 Remainder 0.033 4.167 18.7 4 26.8 9.1 1.2 8.7 Remainder 0.052 8.648 10 5 22.8 7.7 0.4 10.8 Remainder 0.066 10.734 14 6 35.2 8.7 0.2 0.5 Remainder 0.057 0.443 15 7 32.1 9.1 0.4 6.2 Remainder 0.139 6.061 21.5 Radial crushing Rate of Wear Wear strength dimensional Product yield Corrosion resistance resistance Bearing (MPa) change (%) (%) resistance (1) (2) Invention 1 205 0.9 A A A A Example 2 215 0.3 A A A A 3 193 0.8 A A A A 4 177 1.0 B A A A 5 202 1.2 B A A A 6 184 0.5 A A A A 7 238 0.8 A A A A 8 240 1.0 A A A A 9 219 1.3 B A A A 10 232 1.1 A A A A 11 264 1.4 B A A A 12 259 1.2 A A A A 13 278 1.0 A A A A 14 276 0.8 A A A A 15 268 1.1 A A A A Comparative 1 191 0.3 A C A A Example 2 176 1.1 B C C C 3 297 1.7 C A A A 4 211 1.7 C A A A 5 98 2.0 C A C C 6 413 0.3 B A C C 7 305 2 C A A A Symbols and ranges of product yield A: >96%, B: 90% to 96%, C: <90% Wear resistance (1): Each of bearings of invention examples and comparative examples was assembled into a fuel pump and a durability test was conducted. Wear resistance (2): Each of bearings of invention examples and comparative examples was assembled into a recirculation exhaust gas flow-rate adjustment valve and a durability test was conducted.

[0098] Table 1 shows the blending composition at the time of preparing samples of the examples, the amount of Combined C in the CuNi alloy powder, the amount of Free C in the sintered material, and the sintering temperature.

[0099] In the samples of Examples Nos. 1 to 15, Combined C in the CuNi alloy powder was, by mass %, 0.001% to 0.07%.

[0100] It can be seen that the samples of Examples Nos. 1 to 15 were sintered sliding materials having good product yield due to a low rate of dimensional change, high radial crushing strength, excellent corrosion resistance and wear resistance.

[0101] Further, the sintered sliding materials shown in the results of Table 2 were sintered sliding materials having a composition including, by mass %, 10.1% to 32.6% of Ni, 5.1% to 11.7% of Sn, 0% to 0.8% of P, and 4.2% to 8.8% of C, with a remainder of Cu and inevitable impurities, the sintered sliding materials were sintered bodies of CuNi alloy grains, the sintered sliding materials had a structure in which pores are dispersedly formed in grain boundaries of a plurality of the alloy grains, and C was contained at an amount of, by mass %, 0.003% to 0.068% in a metal matrix including (consisnting of) the alloy grains.

[0102] With regard to the sample of Comparative Example No. 1, the amount of Ni was small, and the corrosion resistance was poor.

[0103] With regard to the sample of Comparative Example No. 2, the amount of Sn was small, and both of the corrosion resistance and the wear resistance were poor.

[0104] With regard to the sample of Comparative Example No. 3, the amount of Sn was excessively large, and the rate of dimensional change was high and the product yield was poor.

[0105] With regard to the sample of Comparative Example No. 4, the amount of P was excessively large, and the rate of dimensional change was high and the product yield was poor.

[0106] With regard to the sample of Comparative Example No. 5, the amount of C was excessively large, and the product yield was poor due to a high rate of dimensional change and the crushing strength was low.

[0107] With regard to the sample of Comparative Example No. 6, the amount of Ni was large and the amount of C was excessively small. The wear resistance was poor due to the small amount of C. Regarding the amount of Ni, in the case where a sample contains a large amount of expensive Ni, it becomes a material with high cost.

[0108] With regard to the sample of Comparative Example No. 7, the amount of C in grains of of the sintered material was large, and the amount of C was excessively large. The rate of dimensional change was high and the product yield was poor.

[0109] From the above-described results, it can be seen that as long as the samples of the examples satisfy the above-described conditions, it is possible to provide a sintered sliding material having good yield due to a low rate of dimensional change, high radial crushing strength, excellent corrosion resistance and wear resistance.

REFERENCE SIGNS LIST

[0110] 1: bearing member

[0111] 2: fuel pump

[0112] 3: casing

[0113] 5: motor (armature)

[0114] 6: rotating shaft

[0115] 7: impeller

[0116] 8: intake port

[0117] 9: delivery port

[0118] 11: alloy grain

[0119] 12: pore

[0120] 13: free graphite

[0121] 15: exposed portion