Sliding member and method for manufacturing a sliding member

Abstract

To take countermeasures against exposure of a lining.SOLUTION: A slide member comprises: a lining composed 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, where a mass percent concentration of Sn in the lining is larger at an interface between the lining and the resin coating layer than inside the lining.SELECTED DRAWING: Figure 2

Description

Technical Field

[0001] The present invention relates to a sliding member having a resin coating layer and a method for manufacturing the sliding member.

Background Art

[0002] There is known a sliding bearing having a resin coating layer containing a solid lubricant in a resin binder. For example, in Patent Document 1, a sliding bearing is disclosed in which a polyamideimide resin is a resin binder and molybdenum disulfide or the like is a solid lubricant.

Prior Art Documents

Patent Documents

[0003]

Patent Document 1

Summary of the Invention

Problems to be Solved by the Invention

[0004] In a sliding bearing having a resin coating layer, when wear, peeling, or the like occurs in the resin coating layer and the lining is exposed, seizure may occur. The present invention has been made in view of the above problems, and an object thereof is to take measures against the exposure of the lining.

Means for Solving the Problems

[0005] A sliding member according to an embodiment includes a lining made of an aluminum alloy layer containing Sn, Si, and inevitable impurities, and the balance is composed of Al, and a resin coating layer formed on the lining, wherein the mass% concentration of Sn in the lining is The ratio of the mass percentage of Sn at the interface between the lining and the resin coating layer to the mass percentage of Sn in the cross-section of the lining perpendicular to the interface is between 3.6 and 8.6. .

[0006] In this sliding member, if the lining is exposed due to peeling of the resin coating layer, the shaft, which is the mating material, will be in 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 the case where Sn is not present. And in the sliding member, the lining cross section Rather, if the mass percentage concentration of Sn is higher at the interface between the lining and the resin coating layer, the effect of suppressing frictional resistance between the lining and the mating material can be further enhanced.

[0007] 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.

[0008] interface and cross section It is easy to manufacture an aluminum alloy containing Sn without adjusting the mass % concentration of Sn. It is also easy to apply a resin coating layer to the aluminum alloy. When the resin coating layer is applied to the aluminum alloy and then fired at a temperature above the melting point of Sn, 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 the mass % concentration is cross section It becomes larger. Therefore, according to 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. [Brief explanation of the drawing]

[0009] [Figure 1]This is a perspective view of a sliding member according to an embodiment of the present invention. [Figure 2] This is a diagram illustrating the sweating of Sn at the interface. [Figure 3] This is a diagram illustrating the sweating of Sn at the interface. [Figure 4] This is a diagram illustrating the sweating of Sn at the interface. [Figure 5] This diagram schematically illustrates the sweating of Sn at the interface. [Figure 6] This figure shows the measurement results of the adhesion force corrected for the peeling area. [Figure 7] This figure shows the change in the coefficient of friction according to the ratio of Sn between the interface and the cross-section. [Modes for carrying out the invention]

[0010] Here, embodiments of the present invention will be described in the following order. (1) Configuration of the sliding member: (2) Method for manufacturing sliding members: (3) Examples: (4) Other embodiments:

[0011] (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.

[0012] The sliding member 1 has a structure in which a back metal 10, a lining 11, and an overlay 12 are laminated in this order from the farthest away from the center of curvature. Therefore, the back metal 10 constitutes the outermost layer of the sliding member 1, and the overlay 12 constitutes the innermost layer of the sliding member 1. The back metal 10, the lining 11, and the overlay 12 each have a constant thickness in the circumferential direction. For example, the thickness of the back metal 10 is set to be 1.1 mm to 3.8 mm, and the thickness of the lining 11 is set to be 0.2 mm to 0.4 mm. The back metal 10 is formed of, for example, steel.

[0013] The lining 11 is a layer laminated inside the back metal 10 and is composed of an Al alloy. The lining 11 contains Sn that is softer than Al which is the matrix, and Si that is harder than Al. The mass% concentration of Sn is, for example, 2.0 mass% or more and 15.0 mass% or less. When the mass% of Sn becomes less than 2.0 mass%, the hardness of the lining becomes excessively hard and the conformability deteriorates. When it becomes more than 15.0 mass%, the hardness of the lining becomes excessively small and the fatigue resistance deteriorates. Therefore, in this embodiment, Sn is 2.0 mass% or more and 15.0 mass% or less.

[0014] The mass% concentration of Si is, for example, 0.5 mass% or more and 5.0 mass% or less. When the mass% of Si becomes less than 0.5 mass%, the hardness of the lining becomes excessively small and the fatigue resistance deteriorates. When it becomes more than 5.0 mass%, the hardness of the lining becomes excessively hard and the conformability and seizure resistance deteriorate. Therefore, in this embodiment, Si is 0.5 mass% or more and 5.0 mass% or less.

[0015] The lining 11 may further contain inevitable impurities. The remainder of the lining 11 is Al. The inevitable impurities in the lining 11 are Mg, Ti, B, Pb, Cr, etc., and impurities mixed in refining or scrap are assumed. The content of the inevitable impurities in the lining 11 is, for example, 1.0 mass% or less in total. Of course, the presence or absence and concentration of element addition in the lining 11 are just examples, and inevitable impurities may be included.

[0016] The thickness of the overlay 12 can be various values, and can be, for example, several μm, several tens of μm, etc. Hereinafter, the inner side means the side of the center of curvature of the sliding member 1, and the outer side means the side opposite to the center of curvature of the sliding member 1. The inner surface of the overlay 12 constitutes the sliding surface of the mating member 2.

[0017] The overlay 12 according to the present 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 also be added.

[0018] In the present embodiment, the overlay 12 is composed of a binder resin, molybdenum disulfide particles, and inevitable impurities. In addition, hard materials such as barium sulfate particles and SiC particles may be added. The binder resin is, for example, a polyamideimide resin. The overlay 12 may be formed as a plurality of layers by overcoating or the like.

[0019] In the sliding member 1 according to the present embodiment, the concentration of Sn is different between the interface of the lining 11 and cross section Specifically, at the interface between the lining 11 and the overlay 12, the mass% concentration of Sn is higher than that of the lining 11. The sliding member 1 slides with the mating member 2 with the overlay 12 as the sliding surface. When wear or peeling occurs in the overlay 12 during the sliding process, the lining 11 and the mating member 2 may come into contact with each other. cross section

[0020] Sn is softer than Al which is the matrix. When the mating member 2 contacts Sn, the friction coefficient is considered to be lower than when the mating member 2 contacts the matrix. Therefore, the higher the possibility that the sliding partner with the mating member 2 is Sn, the more the possibility of seizure can be reduced.

[0021] ​Therefore, in this embodiment, at the interface between the lining 11 and the overlay 12, the lining 11 cross section The configuration is such that the mass % concentration of Sn is greater than that. According to this configuration, the interface between the lining 11 and the overlay 12 and the lining 11 cross section If the mass percentage concentration of Sn is the same in both cases, cross section This approach reduces the likelihood of seizing compared to the case where the mass percentage of Sn is large.

[0022] Furthermore, since the silicon contained in the Al alloy is harder than Al, the addition of silicon to the Al alloy has the effect of improving wear resistance. In other words, when wear or peeling occurs in the overlay 12 during the sliding process of the sliding member 1 sliding against the mating material 2, the silicon and the mating material 2 may come into contact, but because silicon is hard, it is possible to suppress wear of the lining 11.

[0023] (2) Method for manufacturing sliding members: 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-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.

[0024] (a) Lining formation process The lining formation step is a step of forming the lining 11. In this embodiment, the lining formation step is a step of forming a substrate in a halved 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.

[0025] Furthermore, 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. In addition, 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, cross section There is no difference in Sn concentration between the interface (surface) and the substrate.

[0026] (b) Pre-coating treatment process 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, such as ultrasonic cleaning using hydrocarbon-based cleaning agents, alcohol, or alkaline electrolyzed water.

[0027] (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. Additionally, 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.

[0028] 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 %,.

[0029] The coating process is carried out, 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 the like.

[0030] (d) Drying process The drying process involves drying the coating applied to the lining 11. For example, it may be dried by hot air drying at 60°C to 120°C for 1 to 60 minutes.

[0031] (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. Note that "sweating" is a phenomenon in which Sn in Al melts above its melting point and seeps out to the surface. By firing in the manner described above, the Sn present inside the lining 11 can be released at the interface. As a result, the mass % concentration of Sn at the interface between the overlay 12 and the lining 11 is cross section It can be made larger than that.

[0032] According to this process, the firing of the overlay 12 and the perspiration of Sn can be carried out in the same process, so that the sliding bearing according to this embodiment can be manufactured with simple thermal control. Furthermore, the cost required for manufacturing can also be reduced. Note that the firing temperature and firing time are determined by the interface and cross section The ratio of the mass percentage concentrations of Sn in these two locations can be changed according to the target ratio value, etc.

[0033] (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 in shape, as it is intended to evaluate the properties of the sliding bearing alloy.

[0034] Figure 2 shows the results of evaluating the amount 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 5kV, 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.

[0035] 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 measurement results for Sn are in the left column, and the measurement results for Mo are in the right column. The Sn and Mo measurement results in the same row are from the same sample. In these measurement results, the vertical direction is the depth direction.

[0036] 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 is 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 appears along the interface. Therefore, it was confirmed that when firing is performed at a temperature above the melting point of Sn, Sn seeps out to the interface due to a sweating phenomenon.

[0037] 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 for 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 10kV and a magnification of 500x to measure the surface of the lining 11. Figure 3 is a COMP image, where the gray becomes closer to white as the amount of Sn increases.

[0038] 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.

[0039] As shown in Figure 3, the unfired sample and the sample fired at 215°C showed relatively few white areas indicating a high Sn concentration. On the other hand, the samples fired at 270°C and the sample fired at 300°C showed relatively many white areas indicating a high Sn concentration. Therefore, it was confirmed that firing at a temperature above the melting point of Sn causes Sn to seep out to the interface through a sweating phenomenon.

[0040] 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 where Sn is 7.0 mass%, Si is 2.7 mass%, and the remainder is Al. This sample is also a flat plate-shaped sample.

[0041] 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 5kV 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.

[0042] 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, the lining 11 cross section In this case, no significant difference in Sn concentration was observed 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 increased 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.

[0043] Figure 6 shows the results of evaluating the adhesion between the lining 11 and the overlay 12. Specifically, a total of five samples, including Comparative Examples 1 to 4 and the Example, were manufactured in a flat plate shape. Comparative Examples 1 to 4 were manufactured by firing at a firing temperature of 205°C, which is lower than the melting point of Sn, for 45 minutes. The Example was manufactured by firing at a firing temperature of 270°C, which is higher than the melting point of Sn, for 30 minutes.

[0044] In the adhesion strength evaluation test, pins were bonded to the overlay 12 of each manufactured sample, and a force was applied through the pins in the direction of peeling off the overlay 12. 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 tester was an autograph, and the pins were controlled to move at a speed of 2 mm / min. The adhesive used to bond the pins to the overlay 12 was epoxy resin.

[0045] 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.

[0046] Figure 6 is a graph plotting the peel-area corrected adhesion force measured as described above, and the Sn concentration is obtained by measuring the surface of the lining 11 that appears after peeling off the overlay 12 by EPMA analysis. 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, if the amount of Sn in the lining 11 simply increases, the adhesion force between the lining 11 and the overlay 12 decreases with the increase in Sn. 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.

[0047] In the example, the Sn concentration at the interface of the lining 11 was approximately 16.5% by mass, but the example was fired at 270°C for 30 minutes, which is above the melting point of Sn. In the initial stages of firing, the amount of Sn released was small, 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 the 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, and as a result, the adhesion force corrected for the peeling area was much greater than the adhesion force corrected for the peeling area shown by the dashed line in Figure 6. Thus, firing the overlay 12 at a temperature above the melting point of Sn can increase the adhesion force between the lining 11 and the overlay 12 compared to firing at a temperature lower than the melting point of Sn.

[0048] Furthermore, in the lining 11, the mass percentage concentration of Sn at the interface between the lining 11 and the overlay 12 is cross section If it is larger than, cross section This allows for a lower coefficient of friction compared to the case of the same concentration, and provides a countermeasure against exposure of the lining 11 due to wear and peeling of the overlay 12.

[0049] Figure 7 shows the mass % of Sn at the interface and cross section This figure shows the results of measuring the coefficient of friction μ for multiple samples in which the ratio of Sn to mass% was varied. Specifically, comparative examples and Examples 1-4 were prepared. Table 1 shows the measurement results for each sample. [Table 1]

[0050] Note that the comparative example is an unfired sample. The firing temperature and firing time for each sample are as follows: Example 1: 230℃, 45 minutes Example 2: 270°C, 45 minutes Example 3: 280℃, 45 minutes Example 4: 300℃, 45 minutes That is the case.

[0051] Each sample is a flat plate-shaped sample comprising a lining 11 and an overlay 12. The lining 11 should be manufactured such that the Sn content is 2.0 mass% or more and 15.0 mass% or less, the Si content is 0.5 mass% or more and 5.0 mass% or less, and the remainder is Al. Note that the mass% of the lining 11 after manufacturing may be less than the amount of Sn and Si added during manufacturing, and this can be adjusted by increasing the amount added during manufacturing to a level higher than the target mass%. Examples 1 to 4 are samples manufactured in this manner, where the mass% of Sn in the cross-section is the value shown in Table 1. The amount of Si added is 3 mass%. For each sample, the overlay 12 was removed, and the interface between the lining 11 and the overlay 12 was observed with the interface exposed. The cross-section was also observed with the lining 11 cut perpendicular to the interface.

[0052] A scanning electron microscope (JEOL Ltd., JSM-6610A) was used to observe the interface and cross-section. For measurements of each surface, the acceleration voltage was 5kV, the magnification was 200x for interface observation, and 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.

[0053] 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

[0054] Table 1 contains the friction coefficient μ for each sample, and Figure 7 is a plot of 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 straight line shown in the figure is the result obtained by linearly approximating the change in the friction coefficient μ with respect to the interface / section ratio, based on the measurement results for each sample.

[0055] As shown in Figure 7, the coefficient of friction μ decreases as the interface / section ratio increases. Therefore, even if wear or peeling occurs in the overlay 12, it is thought that the larger the interface / section ratio of the Sn concentration in the lining 11, the less likely seizing will occur. There is no upper limit to the interface / section ratio, but for example, if the interface / section ratio is set to 10 times or less, the amount of Sn at the interface becomes excessive, which has the effect of preventing a decrease in adhesion between the lining 11 and the overlay 12. Furthermore, for example, if the coefficient of friction μ is to be 0.16 or less, the interface / section ratio may be in the range of 3.6 to 8.6.

[0056] (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 for transmissions, piston pin bushings, and boss bushings. 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. Also, the mass % concentration of Sn at the interface between the lining and the resin coating layer cross section Other manufacturing methods besides those described in the above embodiments may be employed to increase the size. For example, after forming the lining 11, a step may be taken in which Sn is released at the interface of the lining 11 by heat treatment at a temperature above the melting point of Sn, and then the overlay 12 is fired onto the interface. Various other manufacturing methods may also be employed. [Explanation of Symbols]

[0057] 1...Sliding member, 2...Mating material, 10...Backing plate, 11...Lining, 12...Overlay

Claims

1. 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.

2. 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.

3. 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 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.

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