EP3601821A1

EP3601821A1 - Three-material roll-bonded sliding bearing having two aluminium layers

Info

Publication number: EP3601821A1
Application number: EP18716535.2A
Authority: EP
Inventors: Gaetano Fabio Cosentino; Michael Wagner; Tobias Seidling
Original assignee: Federal Mogul Wiesbaden GmbH
Current assignee: Federal Mogul Wiesbaden GmbH
Priority date: 2017-03-29
Filing date: 2018-03-23
Publication date: 2020-02-05
Also published as: JP2020516818A; BR112019017943A2; KR20190127812A; DE102017205338A1; CN110418904A; US20200109744A1; WO2018177919A1

Abstract

The present invention relates to a sliding bearing element having a steel supporting layer onto which a 2-layer composite is applied which consists of an aluminium-based substrate having a layer thickness h_S of 0.2 to 0.4 mm and an aluminium-based sliding layer having a layer thickness h_G of 0.005 to 0.1 mm, wherein the substrate and the sliding layer are joined by roll bonding, and a sliding bearing made from two sliding bearing elements of this kind, which are predominantly used for applications in high-performance engines, principally for connecting-rod bearings, crankshaft main bearings and connecting rod bushes, but also in applications in mounting camshafts and counterbalance shafts as well as transmissions.

Description

THREE-STAGE ROLL PLATED SLIDING BEARING WITH TWO ALUMINUM LAYERS

description

The present invention relates to a sliding bearing element, in particular a plain bearing shell, with a supporting layer made of steel, a 2-layer composite applied thereon consisting of an aluminum-based substrate layer and an aluminum-based sliding layer and a sliding bearing of two such plain bearing elements, which are mainly for use in high-performance engines, mainly for Pleuellager, crankshaft main bearings and connecting rod bushings are used, but also find application in the storage of cam and balance shafts and transmissions.

The aluminum-based bearing metal materials are usually cast as a solid aluminum strip and after forming and heat treatment steps by plating, usually roll cladding, connected to a steel strip. Aluminum-based bearing metals provide better embedding capability over copper-based bearing metals, which is understood to be the ability of the material to entrap and embed foreign particles in the bearing gap, such as by abrasion or contamination. Also, the sliding or at least the emergency running properties of the aluminum bearing metals are regularly better, especially if they have higher tin contents. Therefore, these materials can be used without or with sliding layer. In the first case, this is referred to as a two-substance system or storage, in the second case, a ternary system or storage.

The two-layer system and the three-layer system can, as is known, furthermore have a thin intermediate layer for better adhesion between the steel backing and the bearing metal layer. The bearing metal layer is then regularly together with the intermediate layer first by roll-plating to a Pre-plated layer composite and then the layer composite is also connected by roll-bonding with a steel strip. The intermediate layer usually does not perform any function in the composite except for the adhesion promotion, is often a pure aluminum layer and is therefore not included in the categorization in two-layer and three-layer systems.

Two-layer and three-layer systems are also known which have a polymeric coating (lubricating varnish) as a running-in layer. Also such non-metallic layers are not included in the categorization in two-layer and three-layer systems.

Slide bearing elements made of an aluminum two-component system are known, for example, from DE 102 46 848 A1, DE 103 43 618 B3, DE 10 2005 023 541 A1, DE 10 2009 002 700 B3, DE 10 201 1 003 797, DE 10 201 1 087 880 B3 and US Pat EP 1 522 750 B9. The documents discuss aluminum-based bearing metals whose wear resistance, thermal and fatigue strength are compared with the addition of a plurality of elements selected from Sn, Pb, In, Bi, Si, Zn, Cu, Mg, Mn, Ni, Ti, Co, V and / or Cr should be improved.

The term "strength" generally describes the mechanical resistance that a material opposes to separation or plastic deformation.The strength of a material depends essentially on the structure of the crystal lattice, including dislocations.There are different types of strengths depending on the The so-called "fatigue strength" or "fatigue strength" is a dynamic strength which describes the mechanical resistance of a material against time-varying loads. "Tensile strength" usually becomes comparatively simple Tensile test determined, from which then conclusions can be drawn on the fatigue strength or fatigue strength.

The term "wear resistance" refers to the resistance of a material to mechanical abrasion, which in turn can have different causes: on the one hand, there is the devouring wear, in which two materials formally weld under the frictional heat, which leads to the abrasion of one of the materials Thus, a measure of wear resistance is the hardness of the material, which is understood as the resistance that a material opposes to the mechanical penetration of another body, and which is also relatively easy in any of the numerous known endurance tests can be determined.

With regard to the abovementioned alloy constituents, it is thus generally possible to distinguish between two effects. The so-called soft phases, such as Pb, Sn or Bi, reduce as solid lubricants, possibly even under mixed friction conditions, a galling and wear. The hard or solidifying components, such as Si or intermetallic phases of Al with Mn, Cu, Mn, Zn, depending on their size and distribution, have a strength-increasing effect and due to their hardness also contribute to the reduction of wear.

The document DE 10 2009 002 700 B3 also deals with an aluminum-copper alloy as an intermediate layer whose thickness and hardness are adapted to the properties of the bearing metal layer, in order to achieve a total of plastic flexibility and conformability of the plain bearing shell. Disadvantage of the two-layer systems is generally that the effects of the soft phases on the one hand and the strengthening constituents on the other hand in a layer are partially contrary. The bearing metals used in this case therefore always form a compromise with regard to the properties of the wear resistance and / or the thermal and fatigue strength.

Known plain bearing elements made of an aluminum three-material system, as disclosed, for example, in document WO 2016/023790, have a steel back as supporting layer, at least one bearing metal layer and a sliding layer applied to the bearing metal layer by electroplating or sputtering. This makes it possible to optimize the aluminum alloy of the bearing metal layer, for example, for the demanding use in internal combustion engines, in terms of their strength and at the expense of embedding and wear resistance. The latter properties are taken over by the thus optimized sliding layer. The bearing metal layer must then have emergency running properties at best.

For the sliding layer are chemically or electrochemically (galvanic) or by means of PVD process, in particular sputtering, applied thin metal layers into consideration, see. DE 10 2005 063 324 B4 or DE 10 2005 063 325 B4, wherein here a tin-containing aluminum alloy is applied as a sputtering layer on a substrate made of a copper alloy. Such sliding layers are very thin due to production, which is basically advantageous because they do not have high strength. The fatigue strength of the entire bearing is all the more determined by the strength of the underlying bearing metal or substrate layer, the thinner the sliding layer.

The aforementioned coatings are applied in the slide bearing production on the finished slide bearing. The application of the sliding layer Therefore, the production of these sliding bearings is considerably more expensive. In many cases, an intermediate or barrier layer is additionally provided between the bearing metal layer and the sliding layer as a diffusion barrier, which is likewise usually electrodeposited and further increases the cost of the manufacturing process.

The object of the present invention is therefore to provide a bearing element, in particular a plain bearing shell, which is similarly cost-effective to produce as a two-part bearing and, if possible, has the wear resistance and embedding capability and at the same time the thermal and fatigue strength like a three-part bearing.

The object is achieved by a plain bearing element according to claim 1, comprising a supporting layer made of steel, a two-layer composite applied to the support layer consisting of an aluminum-based substrate layer with a layer thickness of 0.2 to 0.4 mm and an aluminum layer. based sliding layer with a layer thickness of 0.005 to 0.1 mm, wherein the substrate layer and the sliding layer are joined by roller cladding and lead-free.

The plain bearing element according to the invention is based on the fact that not as in the above-mentioned two-layer bearings mediation between wear resistance and fatigue strength takes place within a layer, but that as in the known three-layer bearings, these two material properties are each assigned to a separate layer. While the substrate layer is thus adjusted in the sliding bearing element according to the invention so that it ensures a high fatigue strength, the sliding layer has a very good wear resistance with optimized embedding capacity.

In contrast to the known ternary systems, however, the sliding layer and the bearing metal layer are joined by roll-plating. This facilitates the manufacturing process considerably. In particular, a two-component composite of the overlay layer and the bearing metal layer material can first be prefabricated as a strip before it is applied to the steel support layer. By joining the individual layers by means of roll cladding, a continuous strip production is possible without costly coating processes of the individual, already formed plain bearings. The production of plain bearings is simplified and cheaper.

Since the process-reliable roll cladding usually requires a higher material thickness than the desired sliding layer thickness of 0.005-0.1 mm, unlike, for example, galvanic deposition or sputtering, after the application of the sliding layer, a subsequent machining operation may be required. This can be done very efficiently on flat strip bearing elements, which does not significantly increase the cost of production. For radial bearing elements, such as bearing shells or bushings, reworking takes place on the formed workpiece by drilling / profile drilling or broaching. This process is always required and also takes place in the known three-layer bearings, which is why no additional costs arise in this respect. There, however, the bearing metal layer is machined prior to coating with the overlay material. Interestingly, during profile drilling of eccentric profiles, the post-machining process ensures that the sliding layer has a varying wall thickness profile while the substrate layer has a constant thickness. In the known radial bearings, it is exactly the opposite. The sliding layer thickness of 0.005-0.1 mm given herein refers in such bearings with a varying wall thickness profile to the thinnest point of the sliding layer, wherein the profile thickness difference can be up to 25 μm. Elsewhere, the thickness can therefore exceed 0.1 mm. In an advantageous embodiment, the substrate layer of Gleitlagerele- mentes of a first aluminum alloy, in addition to unavoidable impurities from one or more of the constituents

0.1 to 8.0% by weight of copper,

- 0.1 - 2.0 wt .-% manganese

0.2 to 5% by weight of nickel,

- 1, 0 - 8.0 wt .-% zinc,

0.1-5.0% by weight of magnesium,

0.1 to 2.0% by weight of silicon,

0.05 to 1.0% by weight of chromium,

- 0.05 - 1, 0 wt .-% vanadium

and the rest is aluminum.

In the sliding bearing element according to the invention, the substrate layer ensures a high fatigue strength in a manner known per se, that optionally one or more of the elements Cu, Mn, Ni, Zn, Mg and Si are alloyed as strengthening elements.

In an advantageous embodiment, the first aluminum alloy in combination

- 0.4 - 6.0 wt .-% copper and

- 0.3 - 2.0 wt .-% manganese

on.

Copper forms intermetallic precipitates or phases with aluminum which block dislocations in the crystal lattice and thus increase the strength of the material without reducing the bond strength of the substrate layer to steel backing. It has been shown that with a copper content of 0.4 to 6.0 wt .-% and appropriate annealing treatment just the strength form essential coherent precipitates optimally in terms of size, shape and distribution.

Manganese also forms intermetallic precipitates or phases with aluminum, which in the aluminum alloy lead to an increase in toughness and to a reduction in the intercrystalline susceptibility to cracking. In addition, it serves as a dispersion former. The manganese content is preferably 0.3-2.0% by weight, where the manganese acts recrystallization-inhibiting and is therefore chiefly responsible for the markedly improved thermal stability or heat resistance. As a result, even in the presence of copper, the layer becomes less sensitive to temperature influences, such as prevail in particular in the operation of modern internal combustion engines. In addition, an increased recrystallization temperature in the manufacturing process favors the size and shape of precipitates in general. On the other hand, an excessively high proportion of Mn promotes the formation of so-called incoherent precipitates in the form of brittle AlOMn crystals, which have a negative effect on the strength of the material.

Preferably, the first aluminum alloy further comprises 0.5-3 wt% nickel and 0.05-1.0 wt% vanadium or 0.2-2.5 wt% magnesium and 0.1-2.0 Wt .-% silicon on.

In one case, the nickel in the indicated region produces additional solid solution strengthening by occupying lattice sites in the crystal. Here, the copper content can be chosen lower.

In the other case, the magnesium leads to a better cold curing by coherent precipitates, in particular the Cu / Mg ratio plays an important role. In addition, the two embodiments of the invention have proved to be preferred because they have a very good bond strength to steel support layer with suitable thermal treatment and therefore additionally serve as a good adhesion promoter to the sliding layer.

Preferably, the sliding layer consists of a second aluminum alloy, which in addition to unavoidable impurities from one or more of the constituents

- 1, 0 - 10.0 wt .-% silicon,

- 5.0 - 30.0 wt .-% tin,

- 0.1 - 5.0 wt .-% copper

0.1 to 3.0% by weight of manganese,

- 0.05 - 1, 0 wt .-% vanadium,

0.05 to 1.0% by weight of chromium,

and the rest is aluminum.

Preferably, the second aluminum alloy thereof in combination

- 1, 0 - 6.0 wt .-% silicon,

- 5.0 - 25.0 wt .-% tin and

- 0.3 - 2.5 wt .-% copper

on.

As stated above, the overlay mainly takes over the functions of very good wear resistance and embedability. For this purpose, the tin content in the aluminum alloy specified at 5.0-30.0% by weight, which is high compared with the aluminum alloys of the two-layer systems, and therefore significantly increases the embedding capacity and the dry running capacity of the sliding layer, is to be held responsible. 5% by weight are at least necessary for this, but preferably at least 10% by weight. Only when the upper limit of 30 wt .-% is exceeded, the strength of the sliding layer decreases so much that the layer does not stand up to its own high stress. A higher safety is obtained by maintaining the upper limit of 25 wt .-%, particularly preferably 21, 5 wt% as the upper limit. The high tin content benefits plain bearing elements that operate temporarily under mixed friction conditions, such as, for example, bearings in internal combustion engines with start-stop operation, ie bearings in which no hydrodynamic oil lubrication is ensured in phases. In addition, the alloy can be machined more easily by the tin, whereby in the post-processing of the plain bearing element, the accuracy can be increased, for example when drilling. In addition, the service life of the tools used for reworking is increased. At the same time, the adjustment of the sliding layer in the composition of the substrate layer makes it possible to dispense with those alloying elements which increase the wear resistance and reduce the fatigue strength.

As stated with respect to the substrate layer, copper increases the strength of the alloy due to the formation of intermetallic precipitates, so that the sliding layer also contributes to a limited extent to the increase in load.

The supply of Si particles and their controlled by the heat treatment size and distribution can be lowered Fress inclination or the wear resistance can be significantly improved by precipitation hardening, which is again in mixed friction conditions but also in the "normal" hydrodynamic operation advantage.

Preferably, the silicon is distributed so that 35-70 Si particles> 5 μιτι are found on an area of 0.04 mm ² .

More preferably, the maximum particle size is 35 μιτι. This particle size distribution has proven to be particularly advantageous because the Si hard particles> 5 μηη are sufficiently large to ensure a high wear resistance of the material as hard carrier crystals.

To determine the particle size distribution, a surface section of the bearing metal layer of a specific dimension under a microscope, preferably at 500 × magnification, is considered. In this case, the sliding layer can be viewed in an arbitrary plane, since it is assumed that there is a substantially homogeneous distribution of the Si particles in the layer, or at least that a distribution which is intentional or unintentionally inhomogeneous, that is, for example, gradually increases in one direction. or decreases, at least does not leave the claimed limits. The sliding layer is preferably prepared to the shape that first a flat cut is made. The visible in the surface section Si particles are measured to the shape that their longest recognizable extent is determined and equated to the diameter. Finally, all Si particles are added in the surface section with a diameter> 5 μιτι and the number thereof in the examined total measuring surface based on a standard surface. It is also possible to ascertain and add up the diameters of all Si particles falling into such a class (> 5 μιτι) and to calculate an average value from them.

Preferably, the second aluminum alloy further comprises 0.1-1.5 wt% manganese or 0.05-1.0 wt% vanadium and 0.05-1.0 wt% chromium.

In one case, as in the substrate layer, manganese serves to increase toughness, reduce intergranular susceptibility to cracking, and acts as a dispersion former, as well as a recrystallization-inhibiting agent, and is therefore primarily responsible for improved thermal stability or heat resistance. In the other case, the chrome takes over in parts this function. The chromium content, which is matched to the copper content in the aluminum matrix, is responsible for the heat resistance of the material, which is always required for heavily loaded applications also for the sliding layer. The chromium content of 0.05 to 1, 0 wt .-% has proved to be at a simultaneous Zulegierung of 0.3 to 2.5 wt .-% of copper to be advantageous in the overlay matrix sufficient strength increasing precipitates form. On the other hand, a content of 1, 0 wt .-% should not be exceeded, in turn, not to adversely affect the formability.

Finally, the latter aluminum alloy of the bearing metal layer has 0.05 to 1.0% by weight of vanadium, which in this case inhibits the recrystallization of the matrix material because it raises its recrystallization temperature. Vanadium thus also serves to increase the heat resistance as a result.

In an advantageous embodiment, the substrate layer of the sliding bearing element in the finished state has a Brinell hardness of 50-100 HBW 1/5/30 and / or a tensile strength of 200-300 MPa.

In a further advantageous embodiment of the sliding bearing element, the sliding layer in the finished state has a Brinell hardness of 25-60 HBW 1/5/30 and / or a tensile strength of 100-200 MPa.

As already mentioned above, the tensile strength can be used to determine the fatigue strength or durability of the material. Likewise, hardness is an indicator of wear resistance. From hardness and tensile strength conclusions can be drawn on the processability of the material. It has been shown that with the stated hardnesses and tensile strengths, the material properties of sliding and substrate layer are adjusted so that the bearing element shows no significant or at least lower failures even at maximum thermal stress, peak load peaks and temporary lack of lubrication, as the known two-component bearings , If the hardness of the substrate layer falls below the lower limit value, the risk of plastic deformation of the material increases too much, resulting in the continuous loadability of the entire bearing and resulting in a long-term failure. If it exceeds the upper limit, the material becomes brittle.

The same applies to the sliding layer: If the hardness of the sliding layer falls below the specified lower limit value, then this layer can also plastically deform, which does not directly lead to failure, but shortens the service life of the sliding layer in an unacceptable manner. If it exceeds the upper limit, this is accompanied by a significant decline in embedability.

Furthermore, the invention relates to a sliding bearing shell as an embodiment of the sliding bearing element described above, and in particular a plain bearing shell with a nominal diameter of <100 mm, preferably

<80 mm.

As a "nominal diameter", the inner diameter of a plain bearing composed of two plain bearing shells is designated, of which at least one plain bearing shell is designed according to the invention a less loaded bearing side. The embodiment of the sliding bearing according to the invention makes it possible to combine two different plain bearing shells within such a bearing so that the higher loaded plain bearing shell has the thin sliding layer according to the invention, while the less loaded counter shell of the same plain bearing has a thicker sliding layer at the same total bearing thickness. In principle, the thinner sliding layer is advantageous where high fatigue strength is required, while the thicker sliding layer has a better embedding behavior, thereby reducing the dirt sensitivity of the entire sliding bearing. Thus, the respective properties of the plain bearing shells can be tailored even more precisely to the specific application situation.

The slide bearing element according to the invention will be explained in more detail with reference to the figures and examples. Show it:

Figure 1 shows a basic layer structure of the sliding bearing element according to the invention.

Figure 1 shows schematically a perspective section of a sliding bearing element in the form of a plain bearing shell according to the invention. The sliding bearing shell has a total of three layers. As the lowermost layer, a supporting or supporting layer 10 made of steel is provided. On the carrier layer 10, a substrate layer 12 is applied. On the substrate layer 12, in turn, a sliding layer 14 is arranged. The substrate layer 12 and the sliding layer 14 each have the above-discussed aluminum-based composition. The sliding layer has a thickness of 0.005 to 0.1 mm. The following applies: The thinner the overlay, the higher the contribution of the thicker substrate layer to the fatigue strength. The substrate layer has a thickness hs of 0.2 to 0.4 mm. Two exemplary embodiments of the aluminum alloy of the substrate layer are listed below in Table 1 and two exemplary embodiments of the aluminum alloy of the sliding layer are listed in Table 2.

Table 1: Exemplary composition Substrate layer (parts in% by weight)

Al Cu Mn Ni Mg Zn Cr Si V

S1 REST 0.6 0.6 1, 5 - - - - 0.2

S2 REST 4,5 0,7 - 0,7 - - 0,5 -

Table 2: Exemplary composition Slip layer (% by weight)

Ä1 Sn Cu Si Cr V Mn

G1 REST 21, 5 1, 0 4.0 - - 0.35

G2 REST 10.0 0.8 2.4 0.2 0.2

The tensile strengths and hardnesses of the embodiments listed above are shown in Table 3 below.

Table 3: Hardening and tensile strengths R _{m of} the substrate layers (S1 and S2) and sliding layers (G1 and G2) at different times in the manufacturing process

Before

Before finished

Roll cladding on roll cladding

Final annealing bearing shell aluminum steel

Rm Hardness Rm Hardness Rm Hardness Rm Hardness

[MPa] [HBW] [MPa] [HBW] [MPa] [HBW] [MPa] [HBW]

S1 238 71 166 45 265 75 250 70

S2 190 51 180 48 240 63 225 60

G1 181 55 130 35 175 57 130 38

G2 193 56 146 44 190 59 150 42 The hardness and tensile strengths were determined in accordance with DIN EN ISO 6506 and DIN EN 10002.

The production of the bearing elements according to the invention and in particular the adjustment of the material properties of the aluminum alloys of the substrate layer and the sliding layer are described below.

By individually fine-tuning the composition and process flows in the manufacture of the individual layers, the focus of the properties between load-bearing capacity, fatigue strength and / or sliding properties is set according to the requirement profile of the planned application in the above parameter range.

There is provided a strip material of a first aluminum alloy, which forms the substrate layer in the later composite material, and a strip material of a second aluminum alloy, which forms the sliding layer in the later composite material. As can be seen from Table 3, these materials may initially have similar properties in terms of hardness and tensile strength. The casting of the strip materials is followed by an annealing treatment for homogenization at a temperature between 400 and 550 ° C. In the process, the precipitates of the easily soluble elements dissolve in the alloys, such as copper, magnesium, silicon or zinc, and are distributed uniformly. Overall, the material properties are homogenized. Excrements of the less soluble elements such as manganese coarsen and lose their angular shape (indentation). The strip materials can for example be cast on site and then rolled in alternating annealing and forming steps (rolls) to a desired thickness, for example, 1, 4 to 2 mm into strips. Subsequently, the two strip materials are joined by cold roll plating. The thickness of the layers joined after this first roll cladding is in each case about 0.7 to 1 mm, which corresponds to a degree of deformation of about 50%. This is followed by one or more annealing treatments for recrystallization at a temperature between 200 and 400 ° C for 8 to 15 hours. This reduces internal energy of the dislocations resulting from the deformation by rearrangement and formation of a new grain structure, recrystallization starting at lower temperatures, the greater the cold working and the longer the annealing time. In addition, this leads overall to a decrease in tensile strength and hardness of the individual layers (see Table 3). The fine-grained and ideally completely recrystallized microstructure has the best forming properties.

The two-layer composite thus produced is then likewise applied to a steel strip by means of cold-rolled plating, that is to say added to a three-layer composite, the substrate layer being arranged on the steel layer. This is followed, where appropriate, by further rolling steps in which the thickness of the substrate layer and of the sliding layer is further reduced to a desired final dimension (of the substrate layer). Here, degrees of deformation of at least 50% are achieved, with the proviso that high degrees of deformation are accompanied by better bonding of the two-layer composite to the steel backing. The substrate thickness and the sliding layer thickness are then each about 0.2 to 0.4 mm.

After the roll cladding and individual further rolling steps, a recrystallization annealing can follow again if necessary. At the end of the forming, either after the slab cladding on the steel strip or after or after the further rolling passes, a final annealing at temperatures between 150 and 450 ° C, preferably between 200 and 350 ° C for 4 to 12 hours, in which means by Diffusion is formed a bonding zone between the steel strip and the substrate material, resulting in an improvement of the bond between the layers. In addition, the final annealing serves to set the material properties required above in terms of hardness and tensile strength. Due to the different chemical composition, the temperature of the final annealing can be chosen above or below the recrystallization threshold of one of the two layers, so that optionally at the same time recrystallization also takes place in the corresponding layer. Preferably, the temperature will be selected such that the substrate layer will survive the finish anneal without significant tensile and hardness losses as the slip layer loses hardness.

Finally, from the 3-layer composite material, the bearing element is formed by, for example, cut boards, formed in a next process step to slide bearing shells or bushings and the plain bearing shells or bushings are finally machined, with a final dimension of the sliding layer thickness of 0.005 to 0.1 mm is achieved.

LIST OF REFERENCE NUMBERS

steel backing

substrate layer

Overlay

sliding surface

Thickness of the sliding layer

Thickness of the substrate layer

Claims

claims

1 . Slide bearing element comprising

a supporting layer of steel,

a applied to the support layer 2-layer composite consisting of

a lead-free aluminum-based substrate layer having a

Layer thickness hs of 0.2 to 0.4 mm and

a lead-free aluminum-based sliding layer with a

Layer thickness iG of 0.005 to 0.1 mm,

characterized in that the substrate layer and the sliding layer are joined by roll-plating.

2. plain bearing element according to claim 1, characterized in that the substrate layer consists of a first aluminum alloy, in addition to unavoidable impurities of one or more of the following constituents

0.1 to 8.0% by weight of copper,

- 0.1 - 2.0 wt .-% manganese

0.2 to 5% by weight of nickel,

- 1, 0 - 8.0 wt .-% zinc,

0.1-5.0% by weight of magnesium,

0.1 to 2.0% by weight of silicon,

0.05 to 1.0% by weight of chromium,

- 0.05 - 1, 0 wt .-% vanadium

and the rest is aluminum.

3. plain bearing element according to claim 2, characterized in that the first aluminum alloy in combination

0.4-0.6% by weight of copper, - 0.3 - 2.0 wt .-% manganese

having.

4. plain bearing element according to claim 3, characterized in that the first Aluminiunnlegierung further

- 0.5 - 3 wt .-% nickel and

- 0.05 - 1, 0 wt .-% vanadium

having.

5. plain bearing element according to claim 3, characterized in that the first aluminum alloy further

0.2-2.5% by weight of magnesium and

- 0.1 - 2.0 wt .-% silicon

having.

6. plain bearing element according to one of the preceding claims, characterized in that the sliding layer consists of a second aluminum alloy, in addition to unavoidable impurities of one or more of the following constituents

- 1, 0 - 10.0 wt .-% silicon,

- 5.0 - 30.0 wt .-% tin,

- 0.1 - 5.0 wt .-% copper

0.1 to 3.0% by weight of manganese,

- 0.05 - 1, 0 wt .-% vanadium,

0.05 to 1.0% by weight of chromium,

and the rest is aluminum.

7. plain bearing element according to claim 6, characterized in that the second aluminum alloy in combination

- 1, 0 - 6.0 wt .-% silicon, - 5.0 - 25.0 wt .-% tin and

- 0.3 - 2.5 wt .-% copper

having.

8. plain bearing element according to claim 7, characterized in that the second aluminum alloy further

0.1-1.5% by weight of manganese

having.

9. plain bearing element according to claim 7, characterized in that the second aluminum alloy further

- 0.05 - 1, 0 wt .-% vanadium and

- 0.05 - 1, 0 wt .-% chromium

having.

10. plain bearing element according to one of the preceding claims, characterized in that the substrate layer has a Brinell hardness of 50 - 100 HBW 1/5/30.

1 1. Slide bearing element according to one of the preceding claims, characterized in that the substrate layer has a tensile strength of 200 - 300 MPa.

12. plain bearing element according to one of the preceding claims, characterized in that the sliding layer has a Brinell hardness of 25 - 60 HBW 1/5/30.

13. plain bearing element according to one of the preceding claims, characterized in that the sliding layer has a tensile strength of 100 - 200 MPa.

14. plain bearing element according to one of the preceding claims, characterized in that the sliding bearing element is designed as a plain bearing shell.

15. plain bearing element according to claim 14, characterized in that the sliding bearing shell has a nominal diameter of <100mm.

16 sliding bearing composed of two plain bearing shells, of which at least one sliding bearing shell is formed according to claim 15.