• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
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    • 专利摘要:
    The invention relates to a multilayer plain bearing (1) with a sliding layer (5) made of a tin-base alloy containing 1 wt .-% and 8 wt .-% Sb, 8 wt .-% and 20 wt .-% Cu and optionally at least Elements contains Si, Cr, Ti, Zn, Ag and Fe, wherein the proportion for each of these elements is between 0.1 wt .-% and 2 wt .-%, the Summengehalt of all alloying elements is at most 30% by weight and the Rest Sn forms, wherein at least a portion of the Cu with Sn as copper-rich precipitate in the tin matrix is present with a maximum particle size of 50 nm and / or additionally at least one further element from a second group consisting of Al, Bi and Ni, wherein the Proportion of the at least one further element is between 0.1% by weight and 5% by weight for each of these elements, and wherein the sliding layer (5) containing at least one element of the second element group is deposited with a PVD method, if the particle size of the nanoparticles size r is 50 nm.
    公开号:AT515099A4
    申请号:T50070/2014
    申请日:2014-01-31
    公开日:2015-06-15
    发明作者:Walter Dipl Ing Dr Gärtner；Johann Dipl Ing Dr Nagl；Christian Übleis；Jakob Dipl Ing Fh Zidar
    申请人:Miba Gleitlager Gmbh；
    IPC主号:
    专利说明:

    The invention relates to a multilayer plain bearing having a support layer and a sliding layer, and optionally a bearing metal layer which is arranged on the support layer, and optionally at least one intermediate layer, which is or are arranged between the sliding layer and the support layer, in particular on the bearing metal layer, wherein the Sliding layer consists of a tin-base alloy with a tin matrix, which in addition to tin and antimony, copper and optionally at least one element from a first group consisting of silicon, chromium, titanium, zinc, silver and iron, wherein the proportion of antimony between 1 Wt .-% and 8 wt .-%, the proportion of copper between 8 wt .-% and 20 wt .-%, the proportion of each of the elements silicon, chromium, titanium, zinc, silver, iron between 0.1 wt .-% and 2 wt .-%, and wherein the sum amount of all alloying elements is at most 30 wt .-% and the remainder tin with the production-related impurities b formed, wherein at least a portion of the copper with tin forms a copper-rich hard phase, which is present as an excretion in the tin matrix.
    A foreseeable increase in the ignition pressure for large engines in the future requires a plain bearing solution, which has a lower tendency to fatigue than known plain bearings from previously used materials. At the same time, the fatigue strength is improved, the tendency to eat and the corrosion resistance to heavy-fuel operation are reduced. A corresponding adaptability of the sliding layer to dirt particles and to compensate for manufacturing tolerances of waves is also required.
    The use of tin-based alloys for sliding layers of sliding bearings has already been described in the prior art.
    For example, WO 2009/108975 A1 describes a cadmium-, lead-, arsenic- and chromium-free poured sliding bearing alloy of tin-based white metal, with the exception of unavoidable impurities, containing 4 to 30% by weight of antimony as the main alloying element and 1 to 10% by weight of copper containing at least one element of a cobalt, manganese, scandium and germanium-containing element group in a total concentration of from 0.2 to 2.6% by weight, based on the elements used in this group, and at least one element of a magnesium, nickel, Having a zirconium and titanium-containing element group in a total concentration of 0.05 to 1.7% by weight, based on the elements used in this group, the sum content of antimony and copper being at most 35% by weight for an antimony content corresponding to at least three times the copper content. is. The white metal may have an aluminum content of 0.05 to 2.5 wt .-%.
    EP 2 333 129 A1 describes a multilayer sliding bearing comprising at least one support metal layer, a sliding layer and optionally a bearing metal layer arranged between the sliding layer and the supporting metal layer. Between the bearing metal layer and the sliding layer, an intermediate layer consisting of one or more sub-layers, which are electrodeposited or formed by diffusion, wherein each of the sub-layers of one or more elements of the group chromium, nickel, iron, cobalt, copper and tin contains. The electrodeposited sliding layer consists of a tin-based alloy, which in addition to tin as the main alloying element at least one further element from the group antimony and copper, optionally lead and / or bismuth, and optionally at least one element from a group comprising zirconium, silicon, zinc, nickel and silver , and contains unavoidable impurities derived from the production of the elements, wherein the antimony content is at most 20 wt .-%, the copper content of at most 10 wt .-%, the sum of lead and bismuth maximum 1.5 wt .-%, the sum of copper and antimony at least 2 wt .-% and the sum of zirconium, silicon, zinc, nickel and silver is at most 3 wt .-% and wherein tin is bound in the form of intermetallic phases and free as tin phase with beta-tin grains present, the average size have at least one value in pm, which is calculated according to the formula K = A / (S + 3 * C + O), where K is the mean grain size i μιτι, A is a factor, S is the proportion of antimony in wt .-%, C is the sum of Alloying of copper, silver, nickel, and O is the sum of Alloying of lead, bismuth, zinc, other alloying elements and non-metallic particles in wt .-% , and the factor A has the value 50, in particular 70, preferably 100, and wherein the average grain size denotes the arithmetic mean of the values per grain as a geometric mean of the largest and the smallest dimension of this grain, as seen in a cross section is calculated, with the averaging of the largest in the cross-grain visible grain to smaller grains is proceeded until the sum of the cross-sectional areas of the averaged grains reaches 80% of the total cross-sectional area of all beta-tin grains, the tin grains with beta-tin Structure in the tin-based alloy in any case have a mean grain size of at least 2.5 μιτι. The bearing metal layer can i.a. to be a copper-tin alloy. As a material for the support metal layer steel is described.
    The object of the present invention is to provide a plain bearing for a fast and medium speed running (large) engine, especially a four-stroke diesel engine, for heavy fuel operation.
    It should be noted at this point that a large engine means a motor having a sliding bearing having a diameter of at least 200 mm. Usual sizes are e.g. in the range between 200 mm and 400 mm diameter.
    By the terms "fast-running" or "medium-fast running" is meant in four-stroke diesel engines a speed range of typically 750-1000 U / min and 500-750 U / min.
    The term "heavy fuel operation" is understood to mean an engine that is equipped with
    Heavy oil is operated as fuel.
    The object of the invention is achieved with the multilayer plain bearing mentioned above, in which the copper-rich hard phase is present in the form of nanoparticles with egg ner maximum particle size of 50 nm and / or in which the tin base alloy in addition to tin, antimony and copper and optionally at least one element of the first Group contains at least one further element from a second group consisting of aluminum, bismuth and nickel, wherein the proportion of the at least one further element is between 0.1 wt .-% and 5 wt .-% for each of the elements aluminum, bismuth and nickel and wherein the sliding layer (5) containing at least one of these elements of the second element group is deposited by a PVD method when the particle size of the nanoparticles is greater than 50 nm.
    The advantage here is that the hard nanoparticles of the copper-rich tin phase in the tin matrix have a diffusion-inhibiting effect and prevent grain size growth. Furthermore, the spread of cracks is made more difficult. This increases the hardness and stability of the soft tin base, whereby a high fatigue strength is achieved while maintaining the ductile material properties.
    Alternatively or additionally, by the addition of at least one of the further elements aluminum, bismuth and nickel, a grain refinement can be achieved, should the deposition process on its own not produce the desired particle size. It is thus achieved that no or no significant loss of hardness of the sliding layer occurs during operation of the sliding bearing. As a result, the load capacity of the sliding layer can be improved.
    It is advantageous if both the copper-rich nano-hard particles and aluminum and / or bismuth and / or nickel are incorporated in the sliding layer. However, the aforementioned requirements for a sliding bearing for the mentioned (large) engines can be better met even if either the copper-rich nano-hard particles or aluminum and / or bismuth and / or nickel in the sliding layer are present.
    According to one embodiment, it is provided that the sum amount of all alloying elements in addition to tin is between 10 wt .-% and 25 wt .-%. It can thus be further improved the above-mentioned properties of the sliding layer.
    Preferably, the bearing metal layer consists of a bronze, the bronze according to a preferred embodiment of CuPb4Sn4Zn4, CuPb5Sn5Zn5, CuPb7Sn7Zn4, CuPb9Sn5, CuPb10Sn10, CuPb15Sn7, CuPb22Sn2, CuPb20Sn4, CuPb22Sn8, CuPb24Sn2, CuPb24Sn, CuPb24Sn4, CuSn5Zn, CuAHONi, CuSnIO. (For the composition of all listed alloy variants, a tolerance range of up to 5 percentage points applies, for example CuPb4 ± 2.5% Sn4 ± 2.5% Zn4 ± 2.5%). In particular, with a bearing metal layer of bronze or of these bronzes can be achieved in Mehrstoffgleitlagern with the sliding layer according to the invention improved adaptability of the sliding layer against dirt particles, wherein such a layer of layer metal also has correspondingly good emergency running properties.
    The overlay preferably has a layer thickness in a range of 10 μm to 60 μm in a multilayer plain bearing with bearing metal layer or in a range of 150 μm to 1000 μm in a multi-material plain bearing without bearing metal layer. It is thus achieved that the sliding layer has a good embedding ability of potentially occurring dirt particles during use, without being prone to fatigue fractures.
    In view of the adaptive properties of the sliding layer, it is advantageous if it has a Vickers hardness between 15 HV (0.001) and 70 HV (0.001). As a result, an improved embedability of the sliding layer for dirt particles can be achieved while avoiding spontaneous failure.
    Preferably, the intermediate layer and / or the sliding layer is / are deposited from the gas phase on the bearing metal layer. By slowing down or preventing particle diffusion, it is thus possible to reduce or prevent the coagulation of precipitations and thus to produce structures away from the thermodynamic equilibrium.
    For a better understanding of the invention, this will be explained in more detail with reference to the following figure.
    It shows in a schematically simplified representation:
    Fig. 1 is a multilayer plain bearing in the form of a Flalbschale in side view.
    By way of introduction, it should be noted that the location information chosen in the description, such as the top, bottom, side, etc. related to the immediately described and illustrated figure and to be transferred to a new position analogously to the new situation.
    Fig. 1 shows a multi-layer sliding bearing 1 in the form of a plain bearing half shell in side view. Shown is the preferred embodiment of this multi-layer plain bearing 1, namely a four-layer variant comprising a support layer 2, a bearing metal layer 3 arranged directly on the support layer 2, an intermediate layer 4 arranged directly on the bearing metal layer 3 and a sliding layer 5 arranged directly on the intermediate layer 4.
    This basic structure of such four-layer bearings, as e.g. find use in motor vehicles, is known from the prior art, so that further explanations on this unnecessary. However, it should be mentioned that further layers can be arranged, that is, for example, between the bearing metal layer 3 and the supporting metal layer 2, an adhesive layer or on the sliding layer 5 an inlet layer. Likewise, an antifretting layer can be arranged on the back side of the support layer 2.
    In the context of the invention, the multi-layer sliding bearing 1 can also be designed differently, for example as a bearing bush, as indicated by dashed lines in Fig. 1. Likewise, embodiments such as thrust rings, axially running sliding shoes, or the like are possible. Multilayer plain bearings 1 are also possible which cover an angular range deviating from 180 °, so that the multilayer plain bearing 1 need not necessarily be designed as a half shell, although this is the preferred embodiment.
    The support metal layer 2 is made of a material which gives the multilayer plain bearing 1 the required structural strength, for example, a
    Brass or a bronze. In the preferred embodiment of the multi-layer plain bearing 1, however, it consists of a steel.
    As a bearing metal layer 3 a variety of alloys can be used. Examples of these are aluminum-based bearing metals, e.g. AISn6CuNi, AISn20Cu, AISi4Cd, AICd3CuNi, AISi11Cu, AISn6Cu, AISn40, AISn25CuMn, Al-Si1 ICuMgNi, AIZn4Si. In the preferred embodiment of the multi-layer plain bearing 1, the bearing metal layer 3, however, consists of a bronze due to the higher fatigue strength. In particular, the bearing metal layer 3 is made of a bronze which in addition to copper lead in a proportion of 2 wt .-% to 30 wt .-% and / or tin in an amount of 1 wt .-% to 15 wt .-% and / or Zinc in a proportion of 1 wt .-% to 8 wt .-% and / or aluminum in an amount of 1 wt .-% to 4 wt .-% and / or nickel in a proportion of 1 wt .-% to 4 Wt .-% contains. For example, the bearing metal layer 3 may be formed by CuPb4Sn4Zn4, CuPb5Sn5Zn5, CuPb7Sn7Zn4, CuPb9Sn5, CuPb10Sn10, CuPb15Sn7, CuPb22Sn2, CuPb20Sn4, CuPb22Sn8, CuPb24Sn2, CuPb24Sn, CuPb24Sn4, CuSnOZn, CuAMONi, CuSnIO. For the composition of all listed alloy variants, a tolerance range of up to 5 percentage points applies, as has already been stated above.
    Preferably, the bearing metal layer 3 is made of a bronze which in addition to copper 17 wt .-% to 27% wt .-% lead, 0.5 wt .-% to 8.5 wt .-% tin or in a lead-free variant (< 0.05 wt% lead) contains 3.5 wt% to 7.0 wt% tin and 0.5 wt% to 2.5 wt% zinc.
    The bearing metal layer 3 can be deposited or arranged on the support layer 2 by a conventional method known from slide bearing technology. For example, a bimetal of the support layer 2 and the bearing metal layer 3 can be produced by rolling the bearing metal layer 3. Likewise, the bearing metal layer 3 can be poured onto the support layer 2. Optionally, this bimetal is reshaped and / or machined.
    On the bearing metal layer 3 (or possibly on the support layer 2), the intermediate layer 4 is deposited, in particular from the gas phase, preferably by a cathode sputtering method or an electron beam evaporation method. Since these methods are known in principle from the prior art, reference is made to avoid repetition.
    The intermediate layer 4 is preferably made of nickel or a nickel alloy or iron or an iron alloy, for example a stainless steel. In particular, the intermediate layer 4 is deposited with a layer thickness of at least 0.5 μm, preferably at least 0.8 μm, and at most 3 μm, preferably at most 2.1 μm.
    It is further preferred if the intermediate layer 4 has a hardness which corresponds at most to ten times the hardness of the sliding layer 5. It goes without saying that the same methods are used for the hardness measurements to determine this relation.
    It is also possible to provide a plurality of intermediate layers 4 between the bearing metal layer 3 and the sliding layer 5. For example, it may be advantageous if an intermediate layer 4 made of stainless steel and thereon a further intermediate layer 4 made of nickel are arranged. The intermediate layer 4 of stainless steel may have a layer thickness between 1 pm and 2 pm and the further intermediate layer 4 of nickel may have a layer thickness between 0.1 pm and 0.5 pm.
    The sliding layer 5 consists of a tin-based alloy, which also contains antimony and copper in addition to tin. Optionally, the sliding layer 5 may include at least one of a first group consisting of silicon, chromium, titanium, zinc, silver and iron. Further, preferably, another element of a second group consisting of aluminum, bismuth and nickel is included.
    The proportion of antimony is between 1 wt .-% and 8 wt .-%, in particular between 1 wt .-% and 5 wt .-%. When it is less than 1% by weight, the lubricating layer becomes too soft, thereby deteriorating fatigue strength. On the other hand, the sliding layer becomes too hard in a proportion of more than 8 wt%, so that the adaptability of the sliding layer 5 in the break-in phase is too low.
    The proportion of copper is between 8 wt .-% and 20 wt .-%, in particular between 9 wt .-% and 15 wt .-%. With a proportion of less than 8 wt .-%, the proportion of forming nanoparticles is too small to meet the above-mentioned requirement profile of the sliding layer 5. However, if the proportion of copper exceeds 20% by weight, coarse-grained precipitation of the copper-rich hard phase occurs, as a result of which the desired properties are likewise not achieved.
    The proportion of each of the elements silicon, chromium, titanium, zinc, silver and iron can be between 0.1% by weight and 2% by weight, in particular between 0.25% by weight and 1.5% by weight ,
    Silicon may be added to improve the fatigue strength and to slow down diffusion effects, which may result in layer softening.
    By adding chromium, a slowdown of grain boundary diffusion can be achieved.
    Titanium and iron in turn form hard phases with tin, whereby the fatigue strength of the sliding layer 5 can be improved.
    The addition of zinc or silver results in a grain refining of the microstructure, so that no loss of hardness occurs during operation, and on the other hand, the fatigue strength and load capacity of the sliding layer 5 are improved.
    Shares of these elements outside the limits mentioned lead to a property profile of the sliding layer 5, which does not meet the above requirements.
    The proportion of each of the further elements aluminum, bismuth and nickel may be between 0.1% by weight and 5% by weight, in particular between 0.1% by weight and 3.1% by weight.
    Aluminum reduces the coarseness of the structure and can also improve the fatigue strength of the sliding layer 5.
    By adding nickel, grain refining of the microstructure can be achieved, which, on the one hand, inhibits diffusion such that no loss of hardness occurs during operation and, on the other hand, improves the fatigue strength and load capacity of the sliding layer 5.
    The addition of bismuth refines the microstructure and hinders grain boundary diffusion under the influence of temperature.
    It has been found that proportions of aluminum, bismuth, nickel outside the stated quantitative ranges do not lead to the desired result.
    The sum amount of all alloying elements besides tin is limited to a maximum of 30% by weight, preferably to a proportion of between 10% by weight and 25% by weight. It has been found that sum amounts above the specified quantity ranges lead to brittleness, below too low hardness and fatigue strength of the sliding layer 5.
    The remainder to 100 wt .-% forms tin with the usual, production-related impurities.
    In addition to this preferred four-layer design of the multilayer plain bearing 1, the possibility also exists within the scope of the invention that the sliding layer 5 can be deposited directly on the support layer 2. If appropriate, the support layer 2 may also be a connecting rod in whose eye the sliding layer 5 is deposited.
    In addition, there is the possibility that the multi-layer sliding bearing 1 has the structure supporting layer 2 with bearing metal layer 3 arranged directly thereon and on this directly arranged sliding layer 5.
    The sliding layer 5 is preferably deposited on the intermediate layer 4 from the gas phase. In particular, the vapor deposition is carried out by a Katho densputterverfahren or Elektronenstrahlbedampfungsverfahren Runaway, preferably layer thicknesses of at least 10 μιτι, preferably at least 15 μιτι, and a maximum of 60 μιτι, preferably a maximum of 50 μιτι generated, if a bearing metal layer 3 is arranged. In the absence of a bearing metal layer 3 preferably layer thicknesses of at least 150 μιτι, preferably at least 200 μιτι, and at most 1000 μιτι, preferably generated at most 750 μιτι. For deposition by means of sputtering the following parameters can be used:
    Voltage at the substrate: -150 V to 0 V.
    Atmosphere: argon
    Pressure: 7x10 ^ to 6x10'3 mbar,
    Temperature: 80 to 160 ° C
    Voltage at the targets: -450 V to -800 V
    Deposition by means of a PVD process is preferred because they take place beyond the thermodynamic equilibrium so that particle diffusion and coagulation of precipitates can be prevented. During the deposition of the sliding layer 5, the copper-rich flartophase is formed, which consists of η-bronze (Cu6Sn5). These have a maximum grain size of 50 nm due to the deposition conditions. The particle size of the nanoparticles is preferably between 10 nm and 40 nm.
    Preferably, the tin-base alloys after precipitation have a Vickers hardness between 15 FIV (0.001) and 70 FIV (0.001), more preferably between 35 HV (0.001) and 60 HV (0.001).
    The following sliding layers 5 were produced by means of a PVD process. In this case, plain bearing half-shells were introduced consisting of a steel support layer 2 and a leaded bronze as a bearing metal layer 3 in an electromagnetically generated metal vapor, wherein a sliding layer 5 was applied with a thickness of about 15 μιτι. The generation of the sliding layer 5 can take place both from a single source and at the same time from several sources of the same or different composition.
    Example 1:
    As a sliding layer 5, a layer of the composition SnCul 1Sb3 deposited by means of magnetron sputtering of a single sputtering target was produced (substrate temperature 110 ° C., average coating rate 0.19 pm / min, process gas argon at a pressure of 0.7 Pa, voltage at the substrate -50V, Voltage at the target 480V, target composition SnCu11Sb3). This sliding layer 5 was deposited on an intermediate layer 4 of nickel with a layer thickness of 1 pm.
    Slip layer 5 shows finely dispersed nanoparticles of Cu6Sn5 in the tin phase (minimum / average / maximum size of the 10/25/37 nm nano-precipitates). The layer has a hardness of 42 HV (0.001).
    Example 2:
    As a sliding layer 5, a layer of composition SnCu12Sb4 was deposited by means of magnetron sputtering of two sputtering targets of the same chemical composition on an intermediate layer 4 of stainless steel (X5CrNi18-10) (substrate temperature 135 ° C, average coating rate 1.4 pm / min, process gas argon at a pressure of 3.8 Pa, voltage at the substrate 0V, voltage at the target each 690V). The intermediate layer 4 had a layer thickness of 1.5 pm.
    Slip layer 5 shows finely dispersed nanoparticles of Cu6Sn5 in the tin phase (minimum / average / maximum size of the nano-precipitates 14/34/45 nm). The layer has a hardness of 47 HV (0.001).
    Example 3:
    As a sliding layer 5, a layer of composition SnCu13Sb2Ni1 was deposited by means of magnetron sputtering of two sputtering targets of different chemical composition (target 1: SnSb3, target 2: CuNi8) on an intermediate layer 4 of nickel (substrate temperature 90 ° C, average coating rate 0.52pm / min, process gas Argon at a pressure of 1.5 Pa, voltage at the substrate OV, voltage at the target 1 825V, voltage at target 2 467 V). The intermediate layer 4 had a layer thickness of 2 μm.
    Slip layer 5 shows finely distributed nanoparticles of Cu6Sn5 in the tin phase (minimum / average / maximum size of the nano-precipitates 12/21/38 nm). The layer has a hardness of 50 HV (0.001).
    The intermediate layers 4 were produced by means of magnetron sputtering of individual alloy targets (substrate temperature and process gas pressure see design variants, voltage at the target 640 V, average coating rate 0.5 pm / min).
    Example 4:
    As a sliding layer 5, a layer of the composition SnCu10Sb4Ni1 was produced by electron beam vapor deposition of a steel strip from two sources (direct coating without intermediate layer and bearing metal layer 3). (Source 1: graphite crucible with pure antimony, temperature 720 ° C, electron beam power 5.5kW, source 2 water-cooled copper crucible with SnCu25Ni10, temperature 1400 ° C, electron beam power 80kW). At a feed rate of 0.2 mm / s steel strip was applied a layer thickness of 800pm, after forming and fine boring of the plain bearing, the layer thickness was 650pm.
    Slip layer 5 shows finely dispersed nanoparticles of Cu6Sn5 in the tin phase (minimum / average / maximum size of nano-precipitates 11/29/43 nm). The layer has a hardness of 57 HV (0.001).
    On a testing machine, the dirt compatibility and the fatigue strength of the plain bearing half shells with the respective sliding layer 5 were tested according to the examples 1 to 4 in comparison with materials from the prior art.
    As state of the art materials, the following compositions were prepared:
    Comparative Example A: PbSn18Cu2 electroplated, 15 μm thick slipping layer on lead bronze CuPb22Sn3 (deposition from fluoroborate electrolyte, see Dettner Heinz W., Elze Johannes, Handbook of Electroplating Volume II, Munich: Carl Hansa Verlag 1966, page 863 ff). Experience has shown that this overlay has excellent dirt compatibility with good fatigue strength.
    The layer has a hardness of 14 HV (0.001).
    Comparative Example B: sputtered AISn20Cu1 sliding layer on lead bronze CuPb22Sn3.
    Separation conditions: Substrate temperature 140 ° C, average coating rate 0.7 pm / min, process gas argon at a pressure of 1.5 Pa, voltage at the substrate 0V, voltage at the target 630V. Interlayers by means of magnetron sputtering of nickel target (substrate temperature and process gas pressure such as sliding layer, voltage at the target 640 V, average coating rate 0.5 pm / min).
    The layer has a hardness of 84 HV (0.001).
    Neither in Comparative Example A nor Comparative Example B could be found in the hard phase Nanoausscheidungen with a maximum grain size of 50 nm.
    The casting-technical production of the alloys described does not lead to the formation of nano-precipitates.
    Experience has shown that this overlay has an average soil compatibility with excellent fatigue strength.
    Measuring method for determining the grain size of the nano-precipitates: For each sample, SEM-FIB images (magnification 50 k, image section 2.4 × 2.4 μm) were subjected to a statistical image evaluation to determine the grain size of the nano-precipitates in the hard phase.
    In the soil compatibility test, the oil is successively contaminated with hard particles under oscillating load with a specific load amplitude of 75 MPa and the amount of dirt measured at the time of spontaneous failure of the bearing shell. As a result, a statement about good nature and dirt compatibility of the sliding layer 5 can be made.
    The fatigue test was carried out with a swelling load and a specific load amplitude of 75 MPa over 3 million load cycles at a sliding speed of 12 m / s. After the test, the half-shells were measured and the wear of the sliding layer 4 was determined. The fatigue strength of the sliding layer 5 was visually evaluated. The optical rating of 1 to 5 covers the condition of very good (1: running tracks) to very bad (5: large, strong fatigue breaks).
    The results are summarized in Table 1.
    Table 1:
    Table 1 shows the results, averaged over four experiments. It turns out that with the sliding layers 5 according to Examples 1 to 4 a very good soil compatibility was achieved. At the same time show the sliding layers 5 according to Examples 1 to 4 after long-term stress tests only isolated cracks and no wear beyond the inlet requirement. This combination does not include any of the prior art materials.
    In addition to the examples given above, the further compositions of the sliding layer 5 listed in Table 2 were prepared. All data on compositions in the following Table 2 are to be understood as wt .-%. The remainder to 100 wt .-% each forms tin. The abbreviations ZS and ES stand for an intermediate layer in general or for an intermediate layer 4 made of a stainless steel X5CrNi18-10.
    These examples are to be understood as representative of compositions of the overlay 5 in accordance with the abovementioned quantitative ranges of the alloying elements.
    The sliding layers 5 of Examples 14 to 22 were deposited according to one of the aforementioned PVD methods.
    Table 2
    All alloys were deposited on a composite material consisting of a steel support layer 2 and a bearing metal layer 3 made of CuPb22Sn3 (Example 5 was additionally deposited on a bearing metal layer 3 made of CuZnO.sub.5 - variant b) and the intermediate layer 4 indicated in Table 2. The deposition was carried out by sputtering according to the parameters mentioned above.
    Table 3 summarizes the test results for these examples. The hardnesses are given in HV (0.001). The values for the particle size of the nanoparticles are given as minimum / average / maximum particle size.
    For Examples 14 to 22, the grain size was not determined. These examples are representative of embodiments of the overlay 5 without the nanoparticles having a maximum grain size of 50 nm in the copper-rich hard phase.
    Table 3
    The exemplary embodiments show possible embodiments of the sliding layer 5 or of the multi-layer sliding bearing 1.
    For the sake of order, it should finally be pointed out that, for a better understanding of the structure of the multi-layer plain bearing 1, this or its constituent parts have been shown partly unevenly and / or enlarged and / or reduced in size.
    LIST OF REFERENCES 1 Multilayer plain bearing 2 Support layer 3 Bearing metal layer 4 Intermediate layer 5 Slip layer
    权利要求:
    Claims (7)
    [1]
    1. Multilayer plain bearing (1) with a support layer (2) and a sliding layer (5), and optionally a bearing metal layer (3), which is arranged on the support layer (2), and optionally at least one intermediate layer (4) between the Sliding layer (5) and the support layer (2), in particular on the bearing metal layer (3), is or are, wherein the sliding layer (5) consists of a tin-base alloy with a tin matrix, in addition to tin and antimony, copper and optionally contains at least one element from a first group consisting of silicon, chromium, titanium, zinc, silver and iron, wherein the proportion of antimony between 1 wt .-% and 8 wt .-%, the proportion of copper between 8 wt .-% and 20% by weight and the content of the at least one element is between 0.1% by weight and 2% by weight for each of silicon, chromium, titanium, zinc, silver and iron, and the sum amount all alloying elements maximum 30 wt .-% be carries and the rest tin with the production-related impurities, wherein at least a portion of copper with tin forms a copper-rich hard phase, which is present as precipitation in the tin matrix, characterized in that the copper-rich hard phase in the form of nanoparticles having a maximum particle size of 50 nm is present and / or that additionally at least one further element from a second group consisting of aluminum, bismuth and nickel is contained, wherein the proportion of at least one further element between 0.1 wt .-% and 5 wt .-% for each of the elements Aluminum, bismuth and nickel and wherein the sliding layer (5) containing at least one of these elements of the second element group is deposited by a PVD method, when the particle size of the nanoparticles is greater than 50 nm.
    [2]
    2. multilayer plain bearing according to claim 1, characterized in that the Summengehalt all alloying elements in addition to tin between 10 wt .-% and 25 wt .-% is.
    [3]
    3. multilayer plain bearing (1) according to one of claims 1 or 2, characterized in that the bearing metal layer (3) consists of a bronze.
    [4]
    4. Multilayer plain bearing (1) according to claim 3, characterized in that the bronze of CuPb4Sn4Zn4, CuPb5Sn5Zn5, CuPb7Sn7Zn4, CuPb9Sn5, CuPb10Sn10, CuPb15Sn7, CuPb22Sn2, CuPb20Sn4, CuPb22Sn8, CuPb24Sn2, CuPb24Sn, CuPb24Sn4, CuSnöZn, CuAMONi, CuSnIO.
    [5]
    5. multilayer plain bearing (1) according to one of claims 1 to 4, characterized in that the sliding layer (5) has a layer thickness of at least 10 pm and a maximum of 60 pm in a Mehrstoffgleitlager (1) with a bearing metal layer (3) or at least 150 pm and a maximum of 1000 pm in a Mehrstoffgleitlager (1) without bearing metal layer (3).
    [6]
    6. multilayer plain bearing (1) according to one of claims 1 to 5, characterized in that the sliding layer (5) has a hardness according to Vickers between 15 HV (0.001) and 70 HV (0.001).
    [7]
    7. Multilayer plain bearing (1) according to one of claims 1 to 6, characterized in that the intermediate layer (4) and / or the sliding layer (5) from the gas phase on the bearing metal layer (3) is deposited.
    类似技术:
    公开号 | 公开日 | 专利标题
    AT511196B1|2012-10-15|COMPOSITE BEARING
    AT407532B|2001-04-25|COMPOSITE OF AT LEAST TWO LAYERS
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    同族专利:
    公开号 | 公开日
    KR20150091227A|2015-08-10|
    AT515099B1|2015-06-15|
    KR102250748B1|2021-05-12|
    EP2902526B1|2019-03-06|
    CN104819209A|2015-08-05|
    EP2902526A1|2015-08-05|
    JP6687322B2|2020-04-22|
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    US9435376B2|2016-09-06|
    JP2015148340A|2015-08-20|
    US20150219154A1|2015-08-06|
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    法律状态:
    2016-01-15| PC| Change of the owner|Owner name: MIBA GLEITLAGER AUSTRIA GMBH, AT Effective date: 20151116 |
    2021-09-15| MM01| Lapse because of not paying annual fees|Effective date: 20210131 |
    优先权:
    申请号 | 申请日 | 专利标题
    ATA50070/2014A|AT515099B1|2014-01-31|2014-01-31|Multilayer plain bearings|ATA50070/2014A| AT515099B1|2014-01-31|2014-01-31|Multilayer plain bearings|
    US14/571,613| US9435376B2|2014-01-31|2014-12-16|Multi-layered plain bearing|
    CN201410849932.3A| CN104819209B|2014-01-31|2014-12-31|Multilayer plain bearing|
    KR1020150006715A| KR102250748B1|2014-01-31|2015-01-14|Multi-layered plain bearing|
    EP15152804.9A| EP2902526B1|2014-01-31|2015-01-28|Multi-layer sliding bearing|
    JP2015015304A| JP6687322B2|2014-01-31|2015-01-29|Multi-layer plain bearing|
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