SINTERED BEARING FOR MOTOR-TYPE FUEL PUMP AND PRODUCTION METHOD THEREFOR

Abstract

Provided is a bearing for a motor-type fuel injection pump. This bearing is composed of a Cu—Ni-based sintered alloy, inexpensive and has a superior corrosion resistance and abrasion resistance. The bearing contains 10 to 20% by mass of Ni, 2 to 4.5% by mass of Sn, 0.05 to 0.4% by mass of P, 2 to 7% by mass of C, and a remainder consisting of Cu and inevitable impurities. The bearing has a metal structure where Sn is uniformly dispersed and distributed in a metal matrix, and has a porosity of 7 to 17% where a free graphite is dispersed and distributed in pores.

Claims

1. A sintered bearing for a motor-type fuel pump, comprising: 10 to 20% by mass of Ni; 2 to 4.5% by mass of Sn; 0.05 to 0.4% by mass of P; 2 to 7% by mass of C; and a remainder consisting of Cu and inevitable impurities, wherein the sintered bearing has a metal structure where Sn is uniformly dispersed and distributed in a metal matrix, and has a porosity of 7 to 17% where a free graphite is dispersed and distributed in pores.

2. A method for producing a sintered bearing for a motor-type fuel pump, comprising: a step of blending an elemental Sn powder-containing raw material powder to achieve a composition containing 10 to 20% by mass of Ni, 2 to 4.5% by mass of Sn, 0.05 to 0.4% by mass of P, 2 to 7% by mass of C and a remainder consisting of Cu and inevitable impurities; a step of producing a compact by press-molding the raw material powder; and a step of sintering the compact at a temperature of 880 to 960° C.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0022] FIG. 1 shows an electron micrograph obtained by observing, with SEM, a sectional structure of an alloy in an example 6 of the present invention (Cu: remainder, Ni: 18.5%, Sn: 3%, P: 0.2%, C: 6%).

[0023] FIG. 2 shows an electron micrograph obtained by observing, with SEM, a sectional structure of an alloy in an example 5 of the present invention (Cu: remainder, Ni: 17.7%, Sn: 3%, P: 0.15%, C: 4%); and mapping diagrams of Ni, Sn, C, Cu and P that were obtained by observation with EDX.

[0024] FIG. 3 is a cross-sectional view of a structure of a motor-type fuel pump for a gasoline engine.

DETAILED DESCRIPTION OF THE INVENTION

[0025] The sintered bearing for a motor-type fuel pump of the present invention contains 10 to 20% by mass of Ni, 2 to 4.5% by mass of Sn, 0.05 to 0.4% by mass of P and 2 to 7% by mass of C. The sintered bearing of the invention has a remainder consisting of Cu and inevitable impurities, has a metal structure where Sn is uniformly dispersed and distributed in a metal matrix, and has a porosity of 7 to 17% where a free graphite is dispersed and distributed in pores. Further, due to such composition and others, the sintered bearing of the invention can be produced inexpensively, and exhibit a superior corrosion resistance and abrasion resistance even in a low-quality gasoline containing an organic acid(s).

[0026] In addition, a method for producing the sintered bearing for a motor-type fuel pump of the present invention, includes a step of blending an elemental Sn powder-containing raw material powder to achieve a composition containing 10 to 20% by mass of Ni, 2 to 4.5% by mass of Sn, 0.05 to 0.4% by mass of P, 2 to 7% by mass of C and a remainder consisting of Cu and inevitable impurities; a step of producing a compact by press-molding the raw material powder; and a step of sintering the compact at a temperature of 880 to 960° C. In this way, there can be produced the sintered bearing for a motor-type fuel pump of the present invention that has the metal structure in which Sn is uniformly dispersed and distributed in the metal matrix.

[0027] The composition etc. of the sintered bearing for a motor-type fuel pump of the present invention is described in detail hereunder. Here, contained amounts described below are all expressed as % by mass.

(1) Ni: 10 to 20% by Mass

[0028] Ni forms a Cu—Ni—Sn phase with Sn and Cu when sintered, which imparts a superior corrosion resistance to the bearing. A desired corrosion resistance cannot be achieved when the amount of Ni contained is smaller than 10%. Meanwhile, it is also not preferred when the amount of Ni contained is greater than 20%, because there will only be achieved a small effect of improving corrosion resistance, and a high raw material cost will be incurred.

(2) P: 0.05 to 0.4% by Mass

[0029] P has a function effect of promoting the sinterability of the compact, and thus improving the strength of the matrix. When the amount of P contained is smaller than 0.05%, there will only be achieved a small effect of improving the strength of the matrix. Meanwhile, it is not preferred when the amount of P contained is greater than 0.4%, because more Ni—P phases will be precipitated at the grain boundary, which will then impair corrosion resistance.

(3) Sn: 2 to 4.5% by Mass

[0030] Sn forms a Cu—Ni—Sn phase with Ni and Cu when sintered, which imparts a superior corrosion resistance to the bearing. A desired corrosion resistance cannot be achieved when the amount of Sn contained is smaller than 2%. Meanwhile, it is not preferred when the amount of Sn contained is greater than 4.5%, because a high raw material cost will be incurred.

(4) C: 2 to 7% by Mass

[0031] C is derived from graphite. C mainly exists as a free graphite in the pores dispersed in the matrix, imparts a superior lubricity to the bearing, and thus improves the abrasion resistance thereof. A desired effect cannot be achieved when the amount of C contained is smaller than 2%. Meanwhile, it is also not preferred when the amount of C contained is greater than 7%, because there will only be achieved a small effect of improving abrasion resistance, and the strength of the bearing will rather deteriorate.

(5) Porosity: 7 to 17%

[0032] Pores are dispersed in the matrix, and have an effect of controlling the abrasion of the bearing by moderating a strong friction to which the bearing will be subjected under a high-pressure and high-speed flow of a liquid fuel. Such effect is insufficient when the porosity is lower than 7%. Meanwhile, it is not preferable when the porosity is greater than 17%, because the strength of the bearing will deteriorate.
(6) Metal Structure in which Sn is Uniformly Dispersed and Distributed in Metal Matrix

[0033] By uniformly dispersing and distributing Sn in the metal matrix comprised of Cu—Ni—Sn, a superior corrosion resistance against a low-quality gasoline containing an organic acid(s) can be imparted even with a small amount of Sn of 2 to 4.5% by mass.

[0034] In order to uniformly disperse and distribute 2 to 4.5% by mass of Sn in the metal matrix comprised of Cu—Ni—Sn, conditions for an addition method of Sn and a sintering temperature need to be determined appropriately. As a method for adding Sn, there can be considered a method for adding Sn in the form of an elemental Sn powder; and a method for adding Sn in the form of an alloy powder such as an alloy powder of Cu—Sn and Cu—Ni—Sn. However, a Cu—Ni—Sn alloy powder is not preferable, because the powder itself is hard, which will result in a decrease in compression moldability and make it easier for the compact to break. As compared to a Cu—Sn alloy powder, an elemental Sn powder, when employed, can be dispersed in the metal matrix more favorably, and Sn in such case can be efficiently dispersed and distributed in the metal matrix by setting the sintering temperature to 880 to 960° C.

[0035] Described hereunder are detailed working examples of the sintered bearing for a motor-type fuel pump of the present invention. Here, the present invention shall not be limited to the following working examples, but may be modified in various ways.

Working Example 1

(1) Production of Sintered Bearing for Motor-Type Fuel Pump

[0036] As raw material powders, there were prepared a Cu-25% by mass Ni powder having a particle size of not larger than 100 mesh, a Cu-8% by mass P powder having a particle size of not larger than 250 mesh, an Sn powder having a particle size of not larger than 250 mesh, a graphite powder and an electrolytic Cu powder. These raw material powders were then combined together so as to achieve a composition(s) shown in Table 1. Stearic acid of 0.5% by mass was then added thereto, followed by performing mixing with a V-type mixer for 20 min, and then carrying out press molding under a given pressure so as to obtain a compact. This compact was then sintered at a given temperature of 880 to 960° C. in an endothermic gas (heat-absorbing gas) atmosphere, and was later subjected to sizing, the endothermic gas atmosphere being formed by mixing a natural gas with air and then passing the mixture thereof through a heated catalyst for decomposition and conversion. By these steps, there were produced a bearing of the present invention (referred to as an example(s) of the present invention hereunder) having the composition(s) shown in Table 1 and dimensions of outer diameter: 10 mm×inner diameter: 5 mm×height: 5 mm; and, for comparison purposes, a comparative bearing (referred to as a comparative example hereunder) containing Sn by an amount of smaller than 2%.

TABLE-US-00001 TABLE 1 Change in Maximum mass after abrasion Chemical composition (% by mass) Porosity corrosion test depth Bearing Ni Sn P C Cu % % μm Present 1 10.2 2 0.05 2 Remainder 7.4 −0.87 7.8 intervention 2 12.7 3.5 0.1 3 Remainder 9.6 −0.72 5.1 3 14.1 2.5 0.15 3 Remainder 10.4 −0.70 4.3 4 16.7 3 0.2 3 Remainder 11 −0.55 1.6 5 17.7 3 0.15 4 Remainder 12.7 −0.51 1.0 6 18.5 3 0.2 6 Remainder 15 −0.43 0.8 7 18.5 3 0.2 7 Remainder 16.8 −0.32 2.6 8 19.8 3 0.4 5 Remainder 14 −0.36 0.7 Comparative example1 10.5 1 0.2 2 Remainder 12.2 −1.5 18

(2) Corrosion Resistance Test

[0037] A corrosion resistance test was performed on the bearings of the examples of the present invention and the bearing of the comparative example.

[0038] An organic acid test solution for use as a pseudo low-quality gasoline was prepared by adding to a gasoline a carboxylic acid represented by RCOOH (R is a hydrogen atom or a hydrocarbon group). After heating this organic acid test solution to 60° C., the bearings of the examples of the present invention and the bearing of the comparative example were then immersed in such organic acid test solution for 100 hours. Next, changes in mass before and after immersion in the organic acid test solution were measured. The results thereof are shown in Table 1.

[0039] Changes in mass of the bearings of the examples of the present invention were not higher than 0.87%; a high corrosion resistance was confirmed. In contrast, a change in mass of the bearing of the comparative example was 1.5%; a corrosion resistance significantly inferior to those of the examples of the present invention was confirmed.

(3) Abrasion Resistance Test

[0040] An abrasion resistance test was performed on the bearings of the examples of the present invention and the bearing of the comparative example. The condition(s) for the abrasion resistance test were such that the gasoline flowed at a high speed in a narrow space, and a motor generating such high-speed flow rotated at a high speed as well, thus causing each bearing to be subjected to a high pressure and exposed to the gasoline flowing at the high speed. The bearing was at first to be installed into a fuel pump having exterior dimensions of length: 110 mm×diameter: 40 mm, followed by placing such fuel pump into a gasoline tank. Practical experiments were then performed under conditions of impeller rotation frequency: 5,000 to 15,000 rpm, gasoline flow rate: 50 to 250 L/hour, pressure applied to bearing due to high-speed rotation: 500 kPa at maximum, test time: 500 hours. A maximum abrasion depth in a bearing surface after the test was then measured. The results thereof are shown in Table 1.

[0041] The maximum abrasion depths of the bearings of the examples of the present invention were not larger than 7.8 μm; a high abrasion resistance was confirmed. In contrast, the maximum abrasion depth of the bearing of the comparative example was 18 μm; an abrasion resistance significantly inferior to those of the examples of the present invention was confirmed.

(4) Analysis by Scanning Electron Microscope (SEM)

[0042] A scanning electron microscope (SEM) was used to observe sectional structures of alloys in the examples of the present invention. A magnification for analysis was set to 350 times.

[0043] As a result, in the alloys of the examples of the present invention, it was confirmed that pores were dispersed at a ratio of 7 to 17%, and a free graphite was dispersed as well.

[0044] As one example, FIG. 1 shows an electron micrograph of an alloy in an example 6 of the present invention (Cu: remainder, Ni: 18.5%, Sn: 3%, P: 0.2%, C: 6%).

(5) Analysis by Energy Dispersive X-Ray Spectroscopy (EDX) with Scanning Electron Microscope (SEM)

[0045] With regard to the alloys of the examples of the present invention, an energy dispersive X-ray spectroscopy (EDX) analyzer attached to a scanning electron microscope (SEM) was used to study the distribution of each of the elements Ni, Sn, Cu, P and C in the metal matrix. An analysis condition(s) were such that an accelerating voltage was set to 20 kV, and mapping analysis was then carried out on each of the elements Ni, Sn, Cu, P and C with regard to the sectional structures of the bearings. A magnification for analysis was set to 350 times.

[0046] As a result, in the alloys of the examples of the present invention, it was confirmed that Sn was substantially uniformly dispersed and distributed in a meal matrix composed of Cu—Ni—Sn.

[0047] As one example, FIG. 2 shows an electron micrograph of an alloy in an example 5 of the present invention (Cu: remainder, Ni: 17.7%, Sn: 3%, P: 0.15%, C: 4%); and mapping diagrams of Ni, Sn, C, Cu and P. As shown in the mapping diagram of Sn, it is clear that Sn is substantially uniformly dispersed and distributed in the metal matrix composed of Cu—Ni—Sn.