JP5213791B2 - Slide bearing with back layer - Google Patents

Description

  The present invention relates to a plain bearing having a layer on the back side of a back metal of an internal combustion engine such as an automobile, a marine engine, or a general industrial machine engine.

  In recent years, for the purpose of weight reduction and the like, a housing to which a slide bearing is attached has become thinner and aluminum has become less rigid. For this reason, minute repeated strains accompanying dynamic loads are likely to occur in the housing. For example, in a housing such as a large end portion of a connecting rod of a car engine or a main bearing portion, the weight reduction as described above is achieved. Therefore, an inner surface of the housing and a rear surface of a slide bearing attached to the inner surface of the housing In the meantime, relative micro-collisions and micro-slip are caused with repeated distortion of the housing, which is likely to cause fretting damage. In order to eliminate this phenomenon, for example, in the technique disclosed in Japanese Patent Laid-Open No. 2000-314424 (Patent Document 1) previously proposed by the present applicant, in a plain bearing having a sliding layer on the inner surface of the back metal layer, Heat dissipating performance by forming a phosphate coating on the back of the plain bearing back of the plain bearing that is prone to fretting, while forming a good thermal conductive coating on the back without the phosphate coating There is disclosed a plain bearing that is improved in fretting resistance and non-seizure property.

JP 2000-314424 A (Claim 1)

  The slide bearing disclosed in the above-mentioned prior art document 1 is a conventional general engine, and is a bearing having the above-described back layer, which functioned relatively well against fretting and could be used without damage. However, with the recent progress of higher performance and higher performance of engines, higher rotation and higher load have advanced, and the back layer wear resistance due to fretting in the severe use environment for the back layer that rubs against the mounted housing. Tend to be insufficient in resistance and fatigue resistance. Also, when the temperature increases due to high rotation, the back layer is more worn and the worn material accumulates between the back layer and the housing. There was a drawback that seizure occurred, resulting in damage to the bearing.

  The present invention has been made in view of the above circumstances, and an object of the present invention is to provide a plain bearing having a back layer capable of obtaining high fretting resistance.

In order to achieve the above-described object, in the invention according to claim 1, a slide bearing in which a back layer made of Ni or Cu is provided on the back surface of the back metal layer, and the back metal layer with the back layer provided is rolled and heat-treated. In
When the back layer has a (111) plane X-ray diffraction peak intensity P1, a (200) plane X-ray diffraction peak intensity P2, and a (220) plane X-ray diffraction peak intensity P3,
P1 / (P1 + P2 + P3)> 0.6 (a)
P1 ≧ 3 × P2 and P1 ≧ 10 × P3 (B)
Is satisfied ,
The back layer further has an oxidation amount of 5% by mass or less .

According to a second aspect of the present invention, in the plain bearing according to the first aspect, the back layer has a hardness of HV80 or less .

  In the invention according to claim 1, in the case of Ni or Cu having a crystal structure of fcc, the peak intensity P1 of the (111) plane that is the slip plane of the crystal and the (200) plane that is the plane that becomes the slip resistance. The ratio of the peak intensity P1 of the (111) plane, which is the slip plane to the sum of the peak intensity P3 of the crystal plane and the peak intensity P3 of the peak intensity P2 and (220) plane (the ratio of P1 to the sum of P1, P2, P3) If the (value: P1 intensity ratio) is oriented larger than 0.6, the movement of dislocations when the back layer is deformed can be facilitated. For this reason, it is considered that the frictional resistance between the back surface layer and the housing, for example, at the time of fretting is reduced and the amount of wear is reduced, so that the fretting resistance is improved. As a result, the wear resistance of the back layer and the fatigue resistance of the bearing are improved, and bearing damage can be prevented.

Further , when the peak intensity P1 of the ( 111) plane is 3 times or more of the peak intensity P2 of the (200) plane and 10 times or more of the peak intensity P3 of the (220) plane, the fretting resistance is improved. On the other hand, it can be set as the back layer which has the more suitable orientation state of a slip surface. Therefore, wear due to fretting can be further reduced.

Further, when the oxidation amount of the back surface layer is 5 mass% or less, the influence of brittleness is reduced due to oxidation, it is possible to further reduce the wear due to fretting. Desirably, the oxidation amount of the back layer is preferably 2% by mass or less.
In addition, it can control to the back surface layer used as said orientation state and oxidation amount by giving rolling and annealing to the back surface layer formed by plating.

It is a schematic sectional drawing of the slide bearing which concerns on this embodiment. It is a schematic diagram of the X-ray diffraction graph which shows the relationship of the peak intensity P1, P2, P3 of the back surface layer which concerns on this embodiment. It is explanatory drawing of a hydraulic vibration test.

  Hereinafter, embodiments of the present invention will be described with reference to the drawings. FIG. 1 is a schematic cross-sectional view of a plain bearing according to the present embodiment, and FIG. 2 is a schematic diagram of an X-ray diffraction graph showing the relationship between the peak intensities P1, P2, and P3 of the back layer according to the present embodiment. FIG. 3 is an explanatory diagram of a hydraulic vibration test.

  A plain bearing having the cross-sectional view shown in FIG. 1 is produced as follows. A bearing alloy billet cast with the components of Nerai (in the case of this embodiment, Al-8Sn-2.5Si-1Cu-0.3Mn-0.2V-0.2Fe aluminum bearing alloy layer 4) is produced, The Al foil constituting the layer 3 and the bearing alloy billet are joined and rolled by pressure welding to produce a multilayer aluminum alloy plate 5. Thereafter, the multilayer aluminum alloy plate 5 is superposed on the steel back metal provided with the back layer 6 (Ni or Cu) and pressed, and annealed at 300 to 400 ° C. for several hours, whereby the bearing alloy layer 4 forms the intermediate layer 3. A so-called bimetal 1 formed by bonding to the steel back metal layer 2 is produced. The bimetal 1 is processed into a semi-cylindrical shape to produce a half-shaped slide bearing (half-bearing). Moreover, the back surface layer 6 is provided in the back surface of the steel back metal layer 2 by plating.

  In the plain bearing produced as described above, the multilayered aluminum alloy plate 5 is superimposed on the steel back metal layer 2 provided with the back layer 6 and pressed and annealed, and then processed into a semi-cylindrical shape. A bearing was manufactured. By the above processing on the back layer 6, it is possible to obtain desired values for the P1 intensity ratio, oxidation amount, thickness, and hardness of the back layer 6. For example, by changing the pressure welding (rolling) conditions and annealing (heat treatment) conditions, the P1 strength ratio of the back layer 6 can be adjusted to exceed 0.6, the oxidation amount is 5% by mass or less, the thickness is 0. It can be set to a desired value of 1 to 10 μm and a hardness of HV80 or less. In addition, with respect to abrasion of the back surface layer 6 due to fretting, the back surface layer 6 preferably has a thickness of 0.1 to 10 μm. If the thickness is less than 0.1 μm, the fretting resistance tends to decrease. If the thickness is greater than 10 μm or the hardness is greater than HV80, the wear resistance and fatigue resistance of the back layer due to fretting tend to decrease. The thickness and hardness are preferably in the above-described ranges. Furthermore, the amount of oxidation can be measured by performing surface analysis with an X-ray microanalyzer (EPMA) and quantifying oxygen.

  In the present embodiment, when the back layer 6 is measured by X-ray diffraction, the relationship between the peak intensities P1, P2, and P3 is as shown in the graph of FIG. FIG. 2 shows an X-ray diffraction measurement of the back layer 6 of the sample of Example 1 in Table 1 to be described later. The peak intensity P1 of the (111) plane appearing at an angle of about 44 degrees and an angle of about 52 degrees are shown. Only the peak intensity P2 of the (200) plane and the peak intensity P3 of the (220) plane appearing at an angle of about 77 degrees are displayed. From this graph, when P1 = 1, approximately P2 = 0.125, P3 = 0.050. Therefore, P1 / (P1 + P2 + P3) = 0.85, which satisfies the relationship of P1 ≧ 3 × P2 and P1 ≧ 10 × P3.

  Next, with respect to the plain bearing having the back layer according to the present invention, the test results of the actual product and the conventional product having different P1 strength ratios and oxidation amounts will be described. For Examples 1 to 5 shown in Table 1, as described above, a bearing alloy billet cast with the components of nerai was prepared, and the Al foil and the bearing alloy billet constituting the intermediate layer 3 were joined and rolled by pressure welding. After producing the multilayer aluminum alloy plate 5, the multilayer aluminum alloy plate 5 is superimposed on the steel back metal provided with the back layer 6 made of Ni, and is pressed and annealed at 300 to 400 ° C. for several hours, thereby bearing alloy A bimetal 1 in which the layer 4 is bonded to the steel back metal layer 2 through the intermediate layer 3 is produced, and the bimetal 1 is processed into a semi-cylindrical shape to form a slide bearing having a back layer. And it is set as the back layer 6 which has P1 intensity | strength ratio and oxidation amount as shown in Examples 1-5 by adjusting a rolling reduction, annealing temperature, and annealing time.

  On the other hand, in Comparative Example 1 shown in Table 1, a bearing alloy billet cast with a component of nerai is prepared, and an Al foil constituting the intermediate layer 3 and a bearing alloy billet are joined and rolled by pressure welding to form a multilayer aluminum alloy plate 5 Then, the multi-layer aluminum alloy plate 5 is superposed on the steel back metal and pressed, and annealed at 300 to 400 ° C. for several hours, so that the bearing alloy layer 4 is joined to the steel back metal layer 2 via the intermediate layer 3. A bimetal 1 is produced, and the bimetal 1 is processed into a semicylindrical shape to produce a half bearing. Further, by providing a back layer 6 (Ni) on the steel back metal 2 of the half bearing, a slide bearing having a back layer is obtained. That is, the difference in production between Examples 1 to 5 and Comparative Example 1 is that the back layer 6 is provided on the back surface of the steel back metal layer 2 before the former (Examples 1 to 5) is processed into a halved shape. While the latter (Comparative Example 1) is processed into a halved shape after the latter (Comparative Example 1) is processed, the rear layer 6 is simply rolled to the back layer 6 by providing the back layer 6 on the back surface. The difference is that no heat treatment is performed. For this reason, the P1 intensity ratio in the comparative example 1 is very low compared with Examples 1-5, and is less than 0.6. However, the amount of oxidation is the same in Examples 1 to 3 and Comparative Example 1.

  A vibration test was performed on the above-described Examples 1 to 5 and Comparative Example 1 using a hydraulic vibration tester. In the vibration test, as shown in FIG. 3, the sliding bearings of the examples and comparative examples were attached to a housing simulating the large end of a connecting rod of an automobile engine, and a vibration load W of 30 kN was applied under the conditions shown in Table 2. I went. The evaluation was performed based on ranks 1 to 5 classified according to whether or not damage caused by fretting shown in Table 3 can be visually confirmed (observation with a magnifying glass or the like). That is, rank 1 when there is severe fretting with cracks and rank 2 when there is no cracks but severe fretting is evaluated as fretting damage, rank 3 when there is slight fretting, and slight fretting. Rank 4 in which traces could be confirmed and rank 5 in the absence of fretting were evaluated as having no fretting damage.

  Thus, as shown in the evaluation column on the right side of Table 1, for Examples 1 to 5 in which the P1 strength ratio is more than 0.6, rank 3 in any case where the test temperature is 150 ° C. or 180 ° C. It can be evaluated that there is no fretting damage as described above. Among them, when 4% by mass of Example 4 with an oxidation amount of 5% by mass or less and Example 5 with 10% by mass of 5% by mass or more are compared, Both were evaluated as rank 3 at the test temperature, whereas at the test temperature of 150 ° C., Example 4 was evaluated at rank 4 and Example 5 was evaluated at rank 3, indicating that the oxidation amount was 5% by mass. It can be understood that the following is preferable. Furthermore, when Example 3 of 1% by mass with an oxidation amount of 2% by mass or less was compared with Example 4 of 4% by mass of 2% by mass or more, both were evaluated as Rank 4 at a test temperature of 150 ° C. On the other hand, at the test temperature of 180 ° C., Example 3 is evaluated as Rank 4 and Example 4 is evaluated as Rank 3, so that the oxidation amount is preferably 2% by mass or less. Understandable.

  On the other hand, for Comparative Example 1 in which the P1 strength ratio is 0.6 or less, even if the oxidation amount is much less than 5% by mass, the fretting damage of rank 1 regardless of whether the test temperature is 150 ° C. or 180 ° C. It is evaluated as being.

As is apparent from the detailed description above, in the case of Ni or Cu having a crystal structure of fcc, the peak intensity P1 of the (111) plane which is the slip plane of the crystal and the plane which becomes the slip resistance ( The ratio of the peak intensity P1 of the (111) plane which is the slip plane to the sum of the peak intensity P2 of the (200) plane and the peak intensity P3 of the (220) plane (P1 with respect to the sum of P1, P2 and P3) If the ratio value of the ratio: P1 strength ratio) is oriented larger than 0.6, the wear resistance of the back layer and the fatigue resistance of the bearing can be improved, and bearing damage can be prevented. When the amount of oxidation of the back layer is 5% by mass or less, the influence of embrittlement due to oxidation is reduced, and wear due to fretting can be reduced.
In the above-described embodiment, the result of the back layer made of Ni was shown. However, the same result was obtained in a plain bearing using Cu for the back layer.

1 Bimetal 2 Steel back metal layer 3 Intermediate layer 4 Bearing alloy layer 5 Multi-layer aluminum alloy plate 6 Back layer 7 Slide bearing

Claims (2)

In a slide bearing in which a back layer made of Ni or Cu is provided on the back of the back metal layer, and the back metal layer in the state in which the back layer is provided is rolled and heat-treated ,
When the back layer has a (111) plane X-ray diffraction peak intensity P1, a (200) plane X-ray diffraction peak intensity P2, and a (220) plane X-ray diffraction peak intensity P3,
P1 / (P1 + P2 + P3)> 0.6 (a)
P1 ≧ 3 × P2 and P1 ≧ 10 × P3 (B)
Is satisfied ,
The back bearing further has an oxidation amount of 5% by mass or less . The plain bearing according to claim 1, wherein the back layer has a hardness of HV80 or less .

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