JP7836775B2 - Sliding member and method for manufacturing a sliding member - Google Patents

Description

This invention relates to a sliding member having a resin coating layer and a method for manufacturing the sliding member.

A sliding bearing having a resin coating layer containing a solid lubricant in a resin binder is known. For example, Patent Document 1 discloses a sliding bearing in which polyamide-imide resin is the resin binder and molybdenum disulfide or the like is the solid lubricant.

Japanese Patent Publication No. 2002-61652

In sliding bearings with a resin coating layer, wear or peeling of the resin coating layer can occur, potentially exposing the lining and causing seizure.
This invention has been made in view of the above-mentioned problems, and aims to provide a solution to the exposure of the lining.

A sliding member according to one embodiment comprises a lining made of an aluminum alloy layer containing Sn, Si, and unavoidable impurities, with the remainder being Al, and a resin coating layer formed on the lining, wherein the mass % concentration of Sn in the lining is such that the ratio of the mass % of Sn at the interface between the lining and the resin coating layer to the mass % of Sn in a cross-section of the lining perpendicular to the interface is 3.6 to 8.6 .

In this sliding member, if the lining is exposed due to peeling of the resin coating layer or the like, the shaft, which is the mating material, will be able to come into contact with the lining. Since Sn, being a soft material, has a lower coefficient of friction compared to harder materials, even if the lining is exposed, if Sn is present on the surface of the lining, the frictional resistance between the lining and the mating material will be lower compared to when Sn is not present. Furthermore, if the sliding member is configured such that the mass percentage concentration of Sn is higher at the interface between the lining and the resin coating layer than at the cross-section of the lining, the effect of suppressing frictional resistance between the lining and the mating material can be further enhanced.

Furthermore, a method for manufacturing a sliding member according to one embodiment comprises a lining made of an aluminum alloy layer containing Sn, Si, and unavoidable impurities, with the remainder being Al, and a resin coating layer formed on the lining, the method comprising the steps of forming the lining and applying the material for the resin coating layer to the lining, and curing the resin coating layer by firing at a temperature above the melting point of Sn.

It is easy to manufacture an aluminum alloy containing Sn without adjusting the mass percentage concentration of Sn at the interface and the cross-section . Furthermore, it is easy to apply a resin coating layer to the aluminum alloy. When the resin coating layer is fired at a temperature above the melting point of Sn while the aluminum alloy is coated with the resin coating layer, the resin coating layer hardens and bonds to the lining. In this process, Sn accumulates at the interface between the lining and the resin coating layer due to perspiration, and its mass percentage concentration becomes higher than at the cross-section . Therefore, with the above manufacturing method, it is possible to take measures against the exposure of the lining during the firing process of the resin coating layer.

This is a perspective view of a sliding member according to an embodiment of the present invention. This is a diagram illustrating the sweating of Sn at an interface. This is a diagram illustrating the sweating of Sn at an interface. This is a diagram illustrating the sweating of Sn at an interface. This diagram schematically illustrates the sweating of Sn at the interface. This figure shows the measurement results of the adhesion force corrected for the peeling area. This figure shows the change in the coefficient of friction according to the ratio of Sn between the interface and the cross-section .

Here, embodiments of the present invention will be described in the following order.
(1) Configuration of the sliding member:
(2) Method for manufacturing the sliding member:
(3) Examples:
(4) Other embodiments:

(1) Configuration of the sliding member:
Figure 1 is a perspective view of a sliding member 1 according to one embodiment of the present invention. The sliding member 1 includes a backing plate 10, a lining 11, and an overlay 12. The sliding member 1 is a metal member with a half-shaped form obtained by dividing a hollow cylinder in the diametrical direction, and its cross-section is semi-circular. A sliding bearing A is formed by combining two sliding members 1 to form a cylindrical shape. The sliding bearing A supports a cylindrical mating material 2 (engine crankshaft) in the hollow portion formed inside. The outer diameter of the mating material 2 is formed to be slightly smaller than the inner diameter of the sliding bearing A. Lubricating oil (engine oil) is supplied to the gap formed between the outer circumferential surface of the mating material 2 and the inner circumferential surface of the sliding bearing A. The outer circumferential surface of the mating material 2 slides on the inner circumferential surface of the sliding bearing A.

The sliding member 1 has a structure in which a backing plate 10, a lining 11, and an overlay 12 are stacked in order from furthest from the center of curvature. Therefore, the backing plate 10 constitutes the outermost layer of the sliding member 1, and the overlay 12 constitutes the innermost layer. The backing plate 10, lining 11, and overlay 12 each have a constant thickness in the circumferential direction. For example, the thickness of the backing plate 10 is 1.1 mm to 3.8 mm, and the thickness of the lining 11 is 0.2 mm to 0.4 mm. The backing plate 10 is formed from, for example, steel.

The lining 11 is a layer laminated inside the backing plate 10 and is composed of an Al alloy. The lining 11 contains Sn, which is softer than the Al matrix, and Si, which is harder than Al. The mass percentage concentration of Sn is, for example, 2.0 mass% or more and 15.0 mass% or less. If the mass percentage of Sn is less than 2.0 mass%, the lining becomes excessively hard, and its conformability deteriorates. If it is greater than 15.0 mass%, the lining becomes excessively low, and its fatigue resistance deteriorates. Therefore, in this embodiment, the Sn concentration is set to 2.0 mass% or more and 15.0 mass% or less.

The mass percentage concentration of Si is, for example, 0.5% by mass or more and 5.0% by mass or less. If the mass percentage of Si is less than 0.5% by mass, the hardness of the lining becomes excessively low, and the fatigue resistance deteriorates. If it is greater than 5.0% by mass, the hardness of the lining becomes excessively hard, the conformability deteriorates, and the seizure resistance deteriorates. Therefore, in this embodiment, the Si concentration is 0.5% by mass or more and 5.0% by mass or less.

The lining 11 may also contain unavoidable impurities. The remainder of the lining 11 is Al. Unavoidable impurities in the lining 11 include Mg, Ti, B, Pb, Cr, etc., and are expected to be impurities introduced during refining or scrap production. The content of unavoidable impurities in the lining 11 is, for example, 1.0 mass% or less overall. Of course, the presence or absence and concentration of elements added to the lining 11 are just examples, and unavoidable impurities may be present.

The thickness of the overlay 12 can be set to various values, for example, several micrometers, several tens of micrometers, etc. Hereinafter, "inside" refers to the side of the sliding member 1 that is the center of curvature, and "outside" refers to the side opposite the center of curvature of the sliding member 1. The inner surface of the overlay 12 constitutes the sliding surface of the mating material 2.

The overlay 12 in this embodiment is a layer laminated on the inner surface of the lining 11 and constitutes the resin coating layer of the present invention. Therefore, the boundary between the lining 11 and the overlay 12 corresponds to the interface between the lining and the resin coating layer. The overlay 12 can be made of various resins, and various additives can be added.

In this embodiment, the overlay 12 consists of a binder resin, molybdenum disulfide particles, and unavoidable impurities. Other hard materials such as barium sulfate particles or SiC particles may also be added. The binder resin is, for example, a polyamide-imide resin. The overlay 12 may be formed as multiple layers by methods such as layering.

In the sliding member 1 according to this embodiment, the concentration of Sn differs between the interface and the cross-section of the lining 11. Specifically, the mass percentage concentration of Sn is higher at the interface between the lining 11 and the overlay 12 than at the cross-section of the lining 11. The sliding member 1 slides against the mating material 2 with the overlay 12 as the sliding surface, but if wear or peeling occurs in the overlay 12 during the sliding process, the lining 11 and the mating material 2 may come into contact.

Since Sn is softer than the matrix Al, the coefficient of friction is expected to be lower when the mating material 2 is in contact with Sn than when it is in contact with the matrix. Therefore, the higher the probability that the sliding surface between the mating material 2 and Sn is, the lower the possibility of seizing can be.

Therefore, in this embodiment, the interface between the lining 11 and the overlay 12 is configured such that the mass percentage concentration of Sn is greater at the interface between the lining 11 and the overlay 12 than at the cross-section of the lining 11. This configuration reduces the possibility of seizing compared to cases where the mass percentage concentration of Sn is the same at the interface between the lining 11 and the overlay 12 and at the cross-section of the lining 11, or where the mass percentage of Sn is greater at the cross-section.

Furthermore, since the silicon (Si) contained in the Al alloy is harder than Al, the addition of Si to the Al alloy has the effect of improving wear resistance. That is, if wear or peeling occurs in the overlay 12 during the sliding process of the sliding member 1 against the mating material 2, the Si and the mating material 2 may come into contact. However, because Si is hard, it is possible to suppress wear of the lining 11.

(2) Method for manufacturing the sliding member:
Here, an example of a method for manufacturing the sliding member 1 is described. In this embodiment, the sliding member 1 was manufactured by sequentially performing (a) a lining formation step, (b) a pre-coating treatment step, (c) a coating step, (d) a drying step, and (e) a firing step. Of course, the method for manufacturing the sliding member 1 is not limited to the above steps.

(a) Lining Forming Process The lining forming process is a process for forming the lining 11. In this embodiment, the lining forming process is a process for forming a substrate in a half-split shape in which the backing plate 10 and the lining 11 are joined. For example, a substrate in which the backing plate 10 and the lining 11 are joined may be formed by sintering a material prepared on a plate material corresponding to the backing plate 10 such that Sn is 2.0 mass% or more and 15.0 mass% or less, Si is 0.5 mass% or more and 5.0 mass% or less, and the remainder is Al.

Alternatively, a base material in which the backing plate 10 and the lining 11 are joined may be formed by rolling and joining the backing plate 10 and the lining 11. Furthermore, the base material in which the backing plate 10 and the lining 11 are joined may be processed into a halved shape by machining such as press working or cutting. In the lining 11 formed in this way, there is no difference in Sn concentration between the cross section and the interface (surface).

(b) Pre-coating treatment step The pre-coating treatment step is a surface treatment to improve the adhesion of the overlay 12 (resin coating layer) to the surface of the lining 11. For example, the pre-coating treatment step may include surface processing such as fine boring, surface roughening treatment such as blasting, or chemical treatment such as etching or chemical conversion treatment. Silane coupling treatment or plasma treatment may also be performed. It is preferable to perform the pre-coating treatment step after cleaning the substrate with a cleaning agent. Various cleaning methods can be used, for example, ultrasonic cleaning using hydrocarbon cleaning agents, alcohol, alkaline electrolyzed water, etc.

(c) Coating process The coating process involves applying the material for the overlay 12 to the lining 11. For the coating process, a coating solution is prepared by mixing molybdenum disulfide particles with a polyamide-imide binder resin. In addition, solvents such as N-methyl-2-pyrrolidone or xylene may be used as needed to improve the dispersibility of the molybdenum disulfide particles or to adjust the viscosity of the coating solution.

Here, the molybdenum disulfide particles are mixed into the coating solution so that the volume ratio of the total volume of molybdenum disulfide particles in the overlay 12 is a predetermined volume percentage.

The coating process is performed, for example, by applying the coating liquid to a cylindrical coating roll with a diameter smaller than the inner diameter of the lining 11, and rotating the coating roll on the inner surface of the lining 11. Alternatively, the coating process may be carried out by spray coating, electrodeposition coating, or other methods.

(d) Drying process The drying process is a process of drying the coating liquid applied to the lining 11. For example, it is dried by hot air drying at 60°C to 120°C for 1 to 60 minutes.

(e) Firing Process Furthermore, in this embodiment, the overlay 12 is cured by firing at a temperature above the melting point of Sn contained in the lining 11. That is, the resin constituting the overlay 12 can be cured by firing at a firing temperature of 150 to 300°C for 30 to 60 minutes, for example. Therefore, if the firing is performed at a temperature within the firing temperature range of the resin and above the melting point of Sn, which is 231.9°C, Sn can be released at the interface between the overlay 12 and the lining 11 during the firing process. Release is a phenomenon in which Sn in Al melts above its melting point and seeps out to the surface. With firing as described above, the Sn present inside the lining 11 can be released at the interface. As a result, the mass percentage concentration of Sn at the interface between the overlay 12 and the lining 11 can be made greater than that in the cross-section .

This process allows the firing of the overlay 12 and the saturation of Sn to be carried out in the same process, enabling the manufacture of the sliding bearing according to this embodiment with simple thermal control. Furthermore, the manufacturing cost can be reduced. The firing temperature and firing time can be changed according to the target ratio value, which is the ratio of the mass percentage concentration of Sn at the interface and the cross-section .

(3) Examples:
The following describes the internal and interfacial characteristics of a sample of sliding bearing alloy manufactured using the above method. Figure 2 shows the measurement results for a sample in which the lining 11 contains 7.0 mass% Sn, 2.7 mass% Si, and the remainder is Al. This sample is a flat plate-shaped sample as it is intended to evaluate the properties of the sliding bearing alloy.

Figure 2 shows the results of evaluating the amounts of Sn and Mo in a cross-section perpendicular to the interface between the lining 11 and the overlay 12 in the sample. Specifically, a scanning electron microscope (JEOL Ltd., JSM-6610A) was operated at an acceleration voltage of 5 kV, and the cross-section was measured at a magnification of 1000x. In Figure 2, Sn and Mo are represented in gray, with higher concentrations appearing closer to white.

In Figure 2, the unfired sample, the sample fired at 215°C for 60 minutes, the sample fired at 270°C for 30 minutes, and the sample fired at 300°C for 60 minutes are arranged from top to bottom. The Sn content measurement results are in the left column, and the Mo content measurement results are in the right column. Sn and Mo measurement results in the same row are from the same sample. In these measurement results, the vertical direction represents the depth.

The Mo values shown in the right column reflect the amount of molybdenum disulfide in the overlay 12. Therefore, as shown in Figure 2, the lower end of the area where Mo is no longer observed represents the interface between the lining 11 and the overlay 12. Focusing on the interface identified from the Mo measurement results, no increase in Sn concentration is observed in the unfired sample and the sample fired at 215°C. On the other hand, in the sample fired at 270°C and the sample fired at 300°C, Sn is visible along the interface. Therefore, it was confirmed that firing at a temperature above the melting point of Sn causes Sn to seep out to the interface due to a perspiration phenomenon.

Figure 3 shows the results of evaluating the amount of Sn at the interface for the same four samples as in Figure 2. Specifically, after removing the overlay 12 from each sample, the surface of the lining 11 was measured. The measurement was performed using a scanning electron microscope (JEOL Ltd., JSM-6610A) operated at an acceleration voltage of 10 kV and a magnification of 500x. Figure 3 is a COMP image; the gray becomes closer to white as the amount of Sn increases.

In Figure 3, the unfired sample, the sample fired at 215°C for 60 minutes, the sample fired at 270°C for 30 minutes, and the sample fired at 300°C for 60 minutes are arranged from top to bottom. However, in Figure 3, the measurement results for different surfaces of the same sample are shown in pairs on the same row.

As shown in Figure 3, the unfired sample and the sample fired at 215°C showed relatively few white areas indicating high Sn concentration. On the other hand, the samples fired at 270°C and 300°C showed relatively many white areas indicating high Sn concentration. Therefore, it was confirmed that firing at a temperature above the melting point of Sn causes Sn to seep out at the interface through a sweating phenomenon.

Figure 4 shows the sweating of Sn under different firing conditions than those in Figures 2 and 3. Figure 4 shows the measurement results for a sample in lining 11 containing 7.0 mass% Sn, 2.7 mass% Si, and the remainder being Al. This sample is also a flat plate-shaped sample.

Figure 4 shows the results of evaluating the amount of Sn and Mo at the interface between the lining 11 and the overlay 12 in the sample after firing and peeling off the overlay 12. Specifically, a scanning electron microscope (JEOL Ltd., JSM-6610A) was operated at an acceleration voltage of 5 kV and the interface was measured at a magnification of 1000x. In Figure 4, gray is used to represent areas where the concentration of Sn is closer to white. Figure 4 shows the measurement results for a sample fired at 205°C for 45 minutes, a sample fired at 270°C for 15 minutes, a sample fired at 270°C for 60 minutes, and a sample fired at 280°C for 60 minutes. As shown in Figure 4, the amount of Sn at the interface was lowest at 205°C for 45 minutes, and the amount of Sn increased in the order of 270°C for 15 minutes, 270°C for 30 minutes, and 280°C for 60 minutes. Therefore, it was confirmed that the amount of Sn at the interface increases with higher firing temperatures and longer firing times.

Figure 5 schematically shows the state of Sn at the interface, as can be inferred from Figures 2 to 4. Figure 5 schematically shows the state in which the overlay 12 and the lining 11 are connected in a direction perpendicular to the interface. In Figure 5, the light gray at the top represents the overlay 12, and the dark gray represents the lining 11. The white parts in the lining 11 represent Sn. Si is omitted. According to Figures 2 to 4, no significant difference in Sn concentration is observed in the cross-section of the lining 11 depending on the firing temperature and firing time. On the other hand, at the interface between the lining 11 and the overlay 12, the amount of Sn at the interface increases with higher firing temperatures and longer firing times. Therefore, it is thought that Sn seeps out to the interface due to a sweating phenomenon, and as shown in Figure 5, it is thought that mainly Sn near the interface seeps out to the interface and spreads in the direction of the interface.

Figure 6 shows the results of evaluating the adhesion between the lining 11 and the overlay 12. Specifically, a total of five samples—Comparative Examples 1-4 and the Example—were manufactured in a flat plate shape. Comparative Examples 1-4 were manufactured by firing at a temperature of 205°C, lower than the melting point of Sn, for 45 minutes. The Example was manufactured by firing at a temperature of 270°C, higher than the melting point of Sn, for 30 minutes.

In the adhesion strength evaluation test, pins were bonded to the overlay 12 of each manufactured sample, and a force was applied in the direction of peeling the overlay 12 through the pins. The maximum tensile load was measured a total of five times for each sample, and the adhesion strength evaluation value (peel area corrected adhesion strength (MPa)) was obtained by dividing the maximum tensile load by the peel area, and the average value was obtained. The test apparatus was an autograph, controlled to move the pins at a speed of 2 mm/min. The adhesive used to bond the pins to the overlay 12 was epoxy resin.

The concentrations of Sn in each sample were 7% by mass, 12.5% by mass, 20% by mass, and 100% by mass for Comparative Examples 1 to 4, respectively. The concentration of Sn in the Example was 7% by mass. The concentrations of Si in each sample were 2.7% by mass for Comparative Examples 1 and 2 and the Example, and 0% by mass for Comparative Examples 3 and 4. Note that these concentrations represent the amount added, and do not necessarily correspond to the surface concentrations shown in Figure 6.

Figure 6 is a graph plotting the peel-area-corrected adhesion force measured as described above. The Sn concentration is obtained by EPMA analysis of the surface of the lining 11 that appears after peeling off the overlay 12. Focusing on the comparative example in the graph shown in Figure 6, it can be seen that the peel-area-corrected adhesion force decreases with increasing Sn concentration. Therefore, simply increasing the amount of Sn in the lining 11 reduces the adhesion force between the lining 11 and the overlay 12. In Figure 6, the relationship between the Sn concentration at the interface of the lining 11 and the peel-area-corrected adhesion force in the comparative example is shown by a dashed line.

In the example, the Sn concentration at the interface of the lining 11 was approximately 16.5% by mass. This example involved firing at 270°C for 30 minutes, a temperature above the melting point of Sn. Initially, the amount of Sn released during firing was low, and it is thought that the overlay 12 began to harden when the Sn concentration at the interface between the lining 11 and the overlay 12 was less than 16.5% by mass. Therefore, in this example, it is thought that the Sn concentration at the interface increased after the overlay 12 hardened and began to adhere to the lining 11. As a result, the adhesion force corrected by the peeling area, as shown by the dashed line in Figure 6, was significantly higher. Thus, firing the overlay 12 at a temperature above the melting point of Sn can increase the adhesion between the lining 11 and the overlay 12 compared to firing at a temperature lower than the melting point of Sn.

Furthermore, in the case of the lining 11, if the mass percentage concentration of Sn at the interface between the lining 11 and the overlay 12 is greater than that at the cross-sectional area , the coefficient of friction can be reduced compared to the case where the concentration is the same as at the cross-sectional area , and measures can be taken against exposure of the lining 11 due to wear and peeling of the overlay 12.

Figure 7 shows the results of measuring the coefficient of friction μ for several samples in which the ratio of mass% of Sn at the interface to mass% of Sn at the cross-section was varied. Specifically, comparative examples and Examples 1 to 4 were manufactured. Table 1 shows the measurement results for each sample.

Note that the comparative example is an unfired sample. The firing temperature and firing time for each sample are as follows:
Example 1: 230°C, 45 minutes; Example 2: 270°C, 45 minutes; Example 3: 280°C, 45 minutes; Example 4: 300°C, 45 minutes.

Each sample is a flat plate-shaped sample comprising a lining 11 and an overlay 12. The lining 11 should be manufactured such that its Sn content is 2.0% by mass or more and 15.0% by mass or less, its Si content is 0.5% by mass or more and 5.0% by mass or less, and the remainder is Al. Note that the mass percentage of the lining 11 after manufacturing may be less than the amount of Sn and Si added during manufacturing; this can be adjusted by increasing the amount of additives during manufacturing beyond the target mass percentage. Examples 1 to 4 are samples manufactured in this manner, where the mass percentage of Sn in the cross-section is the value shown in Table 1. The amount of Si added is 3% by mass. For each sample, the overlay 12 was removed, and the interface between the lining 11 and the overlay 12 was observed. The cross-section was also observed when the lining 11 was cut perpendicular to the interface.

A scanning electron microscope (JEOL Ltd., JSM-6610A) was used for observation of the interface and cross-section. For measurements of each surface, the acceleration voltage was 5 kV, the magnification was 200x for interface observation, and the magnification was 1000x for cross-sectional observation. Under these conditions, the elements to be quantitatively analyzed were Sn, Al, Si, and O, and the mass percent concentration of Sn at the interface and cross-section was determined. The ratio of these two is the interface/cross-section ratio.

For each of these samples, the overlay 12 was removed, exposing the interface between the lining 11 and the overlay 12, and the coefficient of friction μ of the interface of the lining 11 in each sample was measured. The coefficient of friction was measured using a Bowden type adhesive sliding tester. The measurement conditions were as follows:
Test ball SUJ2 φ8, sliding speed 0.3 mm/s, measurement length 18 mm, load 1.96 N, temperature room temperature, lubrication state dry, sliding method unidirectional

Table 1 contains the friction coefficient μ for each sample. Figure 7 plots the measurement results for each sample, with the friction coefficient μ on the vertical axis and the interface/section ratio on the horizontal axis. The solid lines in the figure represent the linear approximation of the change in friction coefficient μ with respect to the interface/section ratio, based on the measurement results for each sample.

As shown in Figure 7, the friction coefficient μ decreases as the interface/section ratio increases. Therefore, even if wear or delamination occurs in the overlay 12, a larger interface/section ratio of Sn concentration in the lining 11 is considered to reduce the likelihood of seizing. While there is no upper limit to the interface/section ratio, for example, setting it to 10 times or less results in an excessive amount of Sn at the interface, preventing a decrease in adhesion between the lining 11 and the overlay 12. Furthermore, for example, if the friction coefficient μ is to be 0.16 or less, the interface/section ratio may be set in the range of 3.6 to 8.6.

(4) Other embodiments:
In the above embodiment, a sliding member 1 constituting a sliding bearing A that supports the crankshaft of an engine was exemplified, but the sliding member 1 of the present invention may be used to form sliding bearings A for other applications. For example, the sliding member 1 of the present invention may be used to form radial bearings such as gear bushings, piston pin bushings, and boss bushings for transmissions. Furthermore, the sliding member of the present invention may be a thrust bearing, various washers, or a swash plate for a car air conditioner compressor. In addition, methods other than those in the above embodiment may be used as a manufacturing method to make the mass % concentration of Sn at the interface between the lining and the resin coating layer greater than that of the cross-section . For example, after forming the lining 11, a step may be taken to heat-treat it at a temperature above the melting point of Sn to cause Sn to "sweat" at the interface of the lining 11, and then bake an overlay 12 on the interface. Various other manufacturing methods may also be used.

1…Sliding member, 2…Mating material, 10…Backing plate, 11…Lining, 12…Overlay

Claims (3)

A lining consisting of an aluminum alloy layer containing Sn, Si, and unavoidable impurities, with the remainder being Al,
A sliding member comprising a resin coating layer formed on the lining,
The mass percentage concentration of Sn in the lining is
The mass percentage of Sn at the interface between the lining and the resin coating layer / the mass percentage of Sn in the cross-section of the lining perpendicular to the interface is 3.6 to 8.6 .
Sliding member. The aforementioned lining is,
A material containing 2.0% by mass or more and 15.0% by mass or less of Sn, and 0.5% by mass or more and 5.0% by mass or less of Si,
The sliding member according to claim 1. A lining consisting of an aluminum alloy layer containing Sn, Si, and unavoidable impurities, with the remainder being Al,
A method for manufacturing a sliding member comprising a resin coating layer formed on the lining,
The process of forming the lining,
The process involves applying the resin coating layer material to the lining, and curing the resin coating layer by firing it at a temperature above the melting point of Sn such that the mass % of Sn at the interface between the lining and the resin coating layer / the mass % of Sn in the cross-section of the lining perpendicular to the interface is 3.6 to 8.6.
A method for manufacturing a sliding member, including the following.