• 专利附录
  • 专利说明
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    • 专利摘要:
    The invention relates to a method for producing a sliding bearing element (1) with a support metal, which forms a bearing back side, and a bearing metal, wherein the support metal is formed from a bronze-based alloy. The bearing metal is also made of a bronze-based alloy, the hardness of this bronze-based alloy is at least partially reduced by a heat treatment, so that in the radial direction of the sliding bearing a hardness gradient with increasing hardness in the direction of the back (7) of the sliding bearing element (1) becomes.
    公开号:AT511432A4
    申请号:T60/2012
    申请日:2012-01-20
    公开日:2012-12-15
    发明作者:
    申请人:Miba Gleitlager Gmbh；
    IPC主号:
    专利说明:

    The invention relates to a method for producing a sliding bearing with a support metal, which forms a bearing back side, and a bearing metal, wherein the support metal is formed from a bronze-base alloy and a sliding bearing with a support metal, which forms a bearing back side, and a bearing metal, wherein the Support metal is formed from a bronze-based alloy.
    On the one hand, future engines require higher strengths of bearing shells, i. from the warehouse metal. On the other hand, they must also have correspondingly good tribological properties, which are provided inter alia by additional coatings, good damping properties and sufficient adaptability of the complete bearing system to the shaft or the journal. Known multilayer plain bearings solve these diverging tasks by different layer systems, for example with a steel backing as a carrier and a bearing metal layer applied thereon, for example based on aluminum, as well as a running layer optionally applied thereon. In the prior art, therefore, the property profile of a plain bearing is determined and determined by the selection of the individual layers.
    However, special applications, especially in order to better control Frettingprobieme, but require a bearing backing layer based on a non-ferrous metal. The back metal layer is in direct contact with the bearing mount after installation of the plain bearing half shell. It can due to cyclical, unwanted relative movements of the components to each other with a very small oscillation width at the contact surfaces between the bearing and bearing support, especially at highly loaded conrod bearings, to a Reibverschweißung or Reibkorrosion, i. to a local injury, and thus N2011 / 20600
    come to "seizure" of the plain bearing in the bearing housing. Generally speaking, this damage mechanism is also called fretting.
    It is known to use bronze alloys for the back metal layer instead of steel. For example, AT 502 546 A1 describes a back metal layer of copper alloys, such as brass or bronze.
    It is also known from the prior art to manufacture bearing metal layers from a bronze. For example, DE 20 53 696 A describes a plain bearing made of at least two layers of metallic materials, of which a layer is formed as a bearing journal facing the running layer, wherein the running layer is formed as a hard layer of small thickness and with a layer or a material substantially lower hardness is highlighted. This material may be a lead bronze, a tin bronze, a lead-tin bronze, an aluminum alloy of pure aluminum.
    The bronze alloy, when used as a back metal layer, must have high strength to ensure a sufficient bearing seat in the bearing seat. On the other hand, this high strength has a negative effect on the damping properties and the adaptability of the plain bearing in single-layer plain bearings, ie in plain bearings in which the back metal layer also forms the running layer or layer of layered material.
    DE 15 27 549 B describes a semi-finished product for the production of plain bearing shells with uniformly formed thin running layer in the form of cut boards of two or more multilayer composite material, which are formed into semi-cylindrical bearing shells under pressure on the parting surfaces, wherein the composite material to be processed cups having average thickness values over its width, averaged over the material thickness, such that increased average strength values are provided at those locations where compressive thickening is to be expected upon deformation of the composite material. The composite material may have been subjected to heat treatment and / or rolling to produce areas of differing strength. N2011 / 20600 * «
    It is intended to make a semifinished product for the manufacture of plain bearing shells available, in which the thickening occurring during the molding of the plain bearing shells are avoided from the outset on the carrier layers which establish the strength of the bearing. In this way, in simple composite bearings, the running layer to be applied before forming the bearing, for example white metal layer, can be made thinner to increase the long-term impact strength of the bearing. In Dreistofflagem to be created by the invention, the possibility to apply the subsequent running layer of the bearing even before its forms, thereby to be released from the need for a galvanic application and the associated increased production costs and limitation to electrodepositable alloys. The intermediate layer in plain bearings described in this document can be formed from a bronze. So it is also a multilayer structure of the plain bearing required according to this document.
    The object of the present invention is to provide a plain bearing, which has a lower tendency to fretting and which is simple.
    This object is achieved with the method mentioned above and with the slide bearing mentioned above, wherein the bearing metal is also made of a bronze-based alloy and the hardness of this bronze-based alloy is at least partially reduced by a heat treatment, so that in the radial direction of the Sliding bearing a hardness gradient is formed with increasing hardness toward the bearing back side of the sliding bearing, and wherein the bearing metal, the bearing metal is also formed from a bronze-based alloy, and this bronze-base alloy has a hardness gradient with increasing hardness towards the bearing back side.
    It is advantageous, after both the support metal, so the bearing back metal layer, as well as the bearing metal, which forms the bearing metal layer, are formed from a bronze-based alloy, so that the material compatibility is very high and thus the bond strength can be improved. With the hardness gradient formed at least in some areas by the heat treatment, it is achieved that the bronze-based alloy can be made hard on its own, with the result that corresponding advantages with regard to the fretting problem can be achieved , And that the bronze-base alloy but at the sliding surface, ie the surface on which slides off the component to be stored during operation, at least partially has a reduced hardness, and thus can better fulfill the tasks of damping properties and adaptability. The higher hardness of the bronze-base alloy at the back in particular also with regard to the bronze base alloy forming the support metal and its hardness with regard to Frettingproblematik advantageous since this layer can also be made harder.
    In the preferred embodiment of the invention, the support metal and the bearing metal are single-layered and made of a single bronze-based alloy. The advantage here is that the tasks imposed on the sliding bearing can be met by only a single layer, so that it is possible, the slide bearing as a full bronze bearings, i. form as a monometallic bearing element. It can thus be simplified, the production of such plain bearings, since it is no longer necessary to produce composite materials. As a result, problems with delamination phenomena can also be avoided.
    The heat treatment is preferably carried out by means of a laser or by induction heating. It can thus be treated in a simple manner targeted areas of the surface of the sliding bearing without a large-scale heat treatment must be made, although this is also possible with these methods. It is thus possible with this embodiment of the method to specifically subject only that portion of the sliding bearing surface of a heat treatment, and thus a reduction in the hardness of the alloy, which are required for the tribological properties of the sliding bearing, so that the bronze-base alloy in the residual areas still has a higher hardness, and thus the sliding bearing can be made more resistant to mechanical stress.
    According to a further embodiment variant of the method it can be provided that in an area near the surface during the heat treatment, an N2011 / 20600 additional alloying element is introduced into the bronze-based alloy. It is thus an additional adaptation of the sliding surface in terms of their hardness possible, in particular on the reduction of the hardness of the sliding surface. In addition, the simultaneous introduction of this at least one alloying element with the heat treatment can shorten the process time for producing the sliding bearing.
    According to another embodiment variant of the method, it is provided that the heat treatment is carried out with a heat treatment device which, during the heat treatment, passes over the surface of the bronze-based alloy at a speed selected from a range of 1 m / min to 8 m / min. It can thus be improved a higher homogeneity of the property profile in the treated area.
    It can also be provided that the slide bearing load is simulated on an electronic data processing system, that the pressure distribution in the sliding bearing is determined and that thereafter the hardness gradient is adapted to the pressure distribution. It is thus a targeted training of reduced hardness in the sliding bearing achievable, these areas of reduced hardness can be limited only to the area with low pressure load, so that therefore the remaining areas still have the higher hardness of the base material and thus the sliding bearing higher loads better withstand.
    According to a variant embodiment of the sliding bearing, it is provided that an inlet layer or a lubricating varnish layer is arranged on one of the bearing surfaces in the direction of a radial bearing cross-section opposite sliding surface of the bronze-based alloy in order to prevent the run-in behavior, i. To improve the geometry adaptation of the sliding bearing surface to the surface of the stored component. In the case of an only partial reduction in hardness, it is also achieved in this embodiment that the run-in layer or the anti-friction coating is partially disposed on a hard substrate so that the run-in layer or the anti-friction coating layer, should they not have been abraded in these areas during running-in, also during operation N2011 / 20600 can be effective for a longer period of time, even if the running-in layer or the anti-friction varnish layer are formed with a significantly lower hardness.
    The hardness gradient may be formed to a layer depth selected from a range of 0.5 mm to 5 mm. It is therefore achievable, on the one hand, that in the lower layer depth region, the sliding bearing, viewed in the radial direction, is for the most part made harder, with which the plain bearing better withstands higher loads. On the other hand, however, it is possible in the upper layer depth range to make the hardness gradients flowing more fluidly into the harder zone of the plain bearing, whereby an abrupt change in the properties of the plain bearing is avoided.
    It is thus possible to give the plain bearing better emergency running properties, the softer areas of the plain bearing should be partially worn.
    By "lower layer depth range" is meant the range of 0.5 mm to 0.9 mm. The upper layer depth region, on the other hand, denotes a layer depth from 0.9 mm to 5 mm,
    It is also possible that the hardness gradient is formed in the region of longitudinal end faces of the plain bearing layer with a greater layer depth than in a central region. With this embodiment of the sliding bearing, the known edge-bearer problem can be better counteracted in plain bearings. Here, too, the advantage of the adaptability of the sliding bearing as a result of the heat treatment, since this training of the plain bearing by means of the heat treatment is easily displayed, without special mechanical processing or complex layer structures are required.
    As already stated above, the hardness gradient can be formed only in discrete areas, so that areas of higher hardness are still present on the sliding surface.
    The discrete areas may be formed in the form of strips, whereby a variant of the known from the prior art groove bearing is easily displayed.
    Preferably, in the heat-treated areas by the heat treatment, the structure of the bronze-based alloy is changed, wherein in the heat-treated areas, a cast structure is produced and the sliding bearing in the non-heat treated areas has a rolling structure. In particular, this embodiment of the sliding bearing has been found in practice to be particularly advantageous in terms of tribological behavior.
    Preferably, in this embodiment of the sliding bearing, the bronze base alloy in the heat-treated portion has a grain size of at most 1000 pm, whereby a further improvement of the tribo-corrosion behavior can be achieved since the grain size density in the heat-treated portion is reduced by the large grain size. The grain boundary corrosion, especially in the surface area, can be limited by it
    For a better understanding of the invention, this will be explained in more detail with reference to the following figures.
    Each shows in a schematically simplified representation:
    Figure 1 is a plain bearing half shell in side view.
    Fig. 2a - Fig. 2d shows the top view of the sliding surface of a sliding bearing element of various embodiments;
    3 shows the plan view of the sliding surface of a plain bearing element according to a further embodiment variant;
    Fig. 4
    Fig. 5
    Fig. 6 is a side view of a semi-finished product for the production of a sliding bearing element; the side view of another embodiment of a semi-finished product for producing a sliding bearing element; the side view of another embodiment of a semi-finished product for producing a sliding bearing element;
    Fig. 7 - Fig. 10 different hardness curves. N2011 / 20600
    By way of introduction, it should be noted that in the differently described embodiments, the same parts are provided with the same reference numerals or the same component names, wherein the disclosures contained in the entire description can be mutatis mutandis to the same parts with the same reference numerals or component names. Also, the location information chosen in the description, such as top, bottom, side, etc. related to the immediately described and illustrated figure and are to be transferred to the new situation mutatis mutandis when a change in position.
    Fig. 1 shows a sliding bearing element 1 in the form of a plain bearing half shell.
    The non-closed sliding bearing element 1, in addition to the half-shell design with an angular range coverage of at least approximately 180 e also have a deviating angular range coverage, for example, at least approximately 120 0 or at least approximately 90 so that the sliding bearing element 1 as a third shell, especially for two-stroke diesel engines, or as a quarter shell may be, which are combined with corresponding further bearing shells in a bearing receptacle, wherein the Gleitla-gerelement 1 is preferably installed in the higher loaded area of the bearing receptacle according to the invention.
    But there are also other embodiments of the sliding bearing element 1 possible, for example, a design as a bearing bush.
    The sliding bearing element 1 comprises or consists of a sliding bearing layer 2 which forms a supporting element or a supporting shell for the sliding bearing element 1, so that it is self-supporting. At the same time, this plain bearing layer 2 also forms the sliding layer, so that therefore the plain bearing element 1 in the simplest embodiment variant can also be referred to as a monometallic bearing element or single-layer bearing element.
    The plain bearing layer 2 consists of a bronze-based alloy, as will be explained in more detail below. N2011 / 20600
    According to another embodiment variant of the plain bearing element 1, it can be provided that the plain bearing layer 2 consists of or comprises a first partial layer 3 and a second partial layer 4, as shown in phantom in FIG. In this case, the first partial layer 3 forms the supporting shell and the second partial layer 4 forms the sliding layer of the sliding bearing element 1.
    Also in this case, although the compositions of the bronze-based alloy for the first sub-layer 3 are different from the bronze-base alloy of the second sub-layer 4, the plain bearing member 1 is entirely made of bronze-based alloys.
    In Fig. 1, a further embodiment of the slide bearing element 1 is shown in dashed lines, in which on the plain bearing layer 2, which in turn may have the two sub-layers 3, 4, at least partially, especially in the tribologically particularly stressed areas, or as shown over the entire surface Run-in layer 5 or a lubricating varnish layer, which may also be an inlet layer, arranged and connected to the sliding bearing layer in the region of a sliding surface 6. The sliding surface 6 is that surface of the sliding bearing element 1, which faces a component to be supported, ie in particular a shaft, and a rear side 7 of the sliding bearing element 1 along a radial direction according to arrow 8 is formed opposite.
    The run-in layer 5 may optionally also be made of a bronze-based alloy, in which case this bronze-based alloy has a lower hardness compared to the bronze-base alloy (s) of the plain bearing layer 2.
    However, the running-in layer may also consist of a prior art alloy known for this purpose of adapting the sliding bearing element 1 to the surface of the component to be supported during the running-in phase.
    The lubricating varnish layer may consist, for example, of a lubricating varnish on polyamide-imide ba-sis with graphite and MoS2 as solid lubricants. However, other sliding coatings known from the prior art can also be used. N2011 / 20600 1Ö 'In the event that the sliding bearing layer 2 consists of the at least two partial layers 3, 4 of the bronze-based alloys, the at least two partial layers 3, 4 can be connected to one another by conventional methods known from the prior art, for example, to roll cladding, or by depositing the sub-layer 4 on the sub-layer 3 by means of gas-phase deposition method. Preferably, however, in this embodiment, the at least two partial layers 3, 4 are not made of a sintered material but of a solid material.
    The running-in layer 5 or the anti-friction coating layer can likewise be deposited on the plain bearing layer 2 by conventional methods known from the prior art.
    As already stated above, the plain bearing layer 2 consists of a bronze-based alloy, for example a lead bronze or a lead-tin bronze. However, the plain bearing layer 2 is preferably lead-free, ie. that, except for unavoidable impurities in the raw materials, no lead is contained in this alloy.
    In particular, the plain bearing layer 2 consists of a tin bronze, which in the simplest case in addition to copper as a matrix element of tin in a proportion selected from a range with a lower limit of 1.25 wt .-% and an upper limit of 12 wt .-%, zinc in a proportion selected from a range having a lower limit of 0.25 wt% and an upper limit of 6 wt%, and phosphorus in a proportion selected from a range having a lower limit of 0.01 wt% and an upper limit of 0.5% by weight. In particular, the back metal layer 3 consists of CuSn3-1OZn1-4PO, 05-O, 2, such as e.g. CuSn5Zn1P0,1, CuSn8Zn1P0,1, CuSn10Zn3P0,1, CuSn8Zn4P0,1 or CuSn3Zn3P0,1. Tin bronzes of these compositions have shown, in trial runs in engines, that they have a low tendency to fretting, ie, in direct contact with the steel of the bearing seat. have a high resistance to fretting corrosion. These properties of the tin bronze are significantly better than the corresponding ones of steel. N2011 / 20600
    The tin serves as a main alloying element and leads by Mischkristallverfesti-supply to a basic strength of the copper matrix. At more than 12 wt .-% tin, however, the risk of the formation of brittle intermetallic phases and susceptibility to segregation increases greatly, whereby the structure quality and therefore the properties of the back metal layer are adversely affected. At less than 1.25% by weight, the desired properties of the tin bronze are not achieved or not to the extent desired.
    Zinc can be considered a substitute for tin. In particular, at levels up to 2 wt .-% zinc tin can be replaced in a ratio up to 1: 2 by zinc. Zinc increases strength while maintaining the toughness of the tin bronze, allowing the alloy to be hot and cold formed. Furthermore, zinc leads to better deoxidation of the melt, which in turn has a positive effect on the quality of the melt and, subsequently, the quality of the cast material. The zinc content is limited to a maximum of 6 wt .-%, since with higher zinc levels, the risk of formation of intermetallic phases with copper increases.
    Phosphorus is mainly used as a deoxidizer for the melt. In addition, the addition of phosphorus also allowed a slight increase in the tensile strength and hardness of the tin bronze, with the elongation remaining almost unaffected. However, when the phosphorus content is more than 0.5% by weight, the castability of the tin bronze is deteriorated.
    To further improve these effects, it is preferable that the content of tin is within a range having a lower limit of 3 wt% and an upper limit of 8 wt%, and / or the content of zinc is within a lower limit of 1 Wt .-% and an upper limit of 4 wt .-% and / or the proportion of phosphorus selected from a range with a lower limit of 0.25 wt .-% and an upper limit of 0.4 wt .-%.
    These tin bronzes have both static and dynamic strengths comparable to those of steel.
    Not insignificant is that these tin bronzes can be processed in continuous casting, especially in horizontal continuous casting. They can be used without N2011 / 20600 - 12 -
    Damage cold formed, and also have a sufficient Restum-formvermögen, so that the compression can be performed to make cups without additional measures. In addition, they are rollable. In terms of the environment, it is important that the tin bronzes are lead-free substitutable.
    Preferably, the sum content of tin and zinc is at most 15% by weight.
    Limiting the sum of tin and zinc to this value further reduces the risk of intermetallic phase formation and the risk of segregation. In addition, the castability of the melt is improved because melting with a sum content of tin and zinc of more than 15 wt .-% have a very large solidification interval. In addition, the formability of the casting material is improved, which is particularly advantageous in view of the transformation of the flat, strip-shaped semi-finished product into the shell shape.
    To further improve these effects, preferably the sum content of tin and zinc is limited to a maximum of 13% by weight, or the sum content of tin and zinc is selected from a range with a lower limit of 6% by weight and an upper limit of 12 wt .-%.
    In addition to this basic composition of the tin bronze, it is also possible that at least one further alloying element is included for the formation of micro-alloying systems in the tin bronze or for grain refining. For this purpose, a part of the copper may be replaced to an extent of at most 7 wt .-% by at least one element from a group comprising cobalt, zirconium, manganese, titanium, magnesium, boron, niobium, vanadium, iron, chromium, scandium, and carbon , It can thus be set different microstructure conditions (micro alloying system, grain refining for good formability and high strength, also heat resistance, influencing the tribology by incorporating intermetallic phases as spacers).
    In addition, rare earths in the amount of not more than 0.1 wt .-%, in particular not more than 0.05 wt .-%, may be included in general. N2011 / 20600 -13-
    It can be achieved by cobalt or boron a finer grain structure of the casting alloy. This property can be enhanced by the combined addition of cobalt and boron as expected, which is why an interaction between cobalt and boron in the melt of the tin bronze is suspected.
    Manganese can improve the cold strength and heat resistance of the tin bronze by solid solution hardening. In addition, the recrystallization temperature can be increased.
    By adding titanium to the tin bronze, solidification of the tin bronze can be achieved via precipitation hardening. In particular in connection with carbon, a grain-fine effect can also be achieved, since the carbides act as crystallization nuclei.
    The addition of magnesium can also precipitation hardening by Cu2Mg and thereby an increase in strength of the tin bronze can be achieved.
    This is also true due to the Cu3Zr precipitation phase for the addition of zirconium, and zirconium may also be added to increase the recrystallization threshold of previously work-hardened tin bronzes. By carbide formation, zirconium can also have a fine grain due to the formation of nuclei.
    Niobium or vanadium can be added to the grain refining of the cast structure, whereby again an increase of the effect can be achieved with the simultaneous addition of boron.
    Iron also serves to refine the cast structure, with an increase in the effect of phosphorus or the simultaneous addition of nickel observed.
    By the addition of chromium to the tin bronze, this can be solidified via the hot curing, which eliminates elementary chromium after aging. No intermetallic compounds are formed between Cu and Cr, so that no significant N2011 / 20600 is present due to the addition of chromium to the tin bronze
    Losses in elongation could be detected, despite the increasing strength in the aging annealing.
    Scandium serves to increase the recrystallization threshold after previous cold forming.
    Nickel in combination with phosphorus may be added to grain refining to increase strength and at low levels in combination with phosphorus.
    Cobalt may be contained in a proportion selected from a range having a lower limit of 0.01% by weight and an upper limit of 2.0% by weight and / or manganese in a proportion selected from a range having a lower limit of 0.01 wt% and an upper limit of 0.5 wt%, wherein the sum content of the elements cobalt, zirconium, manganese is preferably selected from a range having a lower limit of 0 , 02 wt .-% and an upper limit of 2.1 wt .-%. The possible amount of zirconium thus results from this sum fraction minus the proportions of cobalt and / or manganese.
    The proportion of cobalt is limited to a maximum of 2.0 wt .-%, in order to avoid segregation during cooling of the melt, whereby the properties of the back metal layer would be degraded by the thereby precipitated phases.
    On the one hand, manganese can be used exclusively for deoxidation (with a proportion of between 0.01% by weight to 0.02% by weight) or above a proportion of 0.02% by weight due to the selected range for the proportion of manganese contribute to increase the strength of the tin bronze. At levels greater than 0.5% by weight, the strength of the tin bronze becomes too high.
    The proportion of zirconium can be between 0.01% by weight and 0.3% by weight, with even small amounts (up to about 0.1% by weight) favoring the formation of a heterogeneous structure and thus contributing to the hardening , In the range between 0.2% by weight and 0.3% by weight, a maximum increase in the recrystallization threshold of previously work-hardened samples was observed. However, even small amounts of zirconium in the range of 0.02% by weight to 0.03% by weight may have a grain-fining effect in combination with carbon, since the carbides formed with carbon act as crystallization nuclei Act.
    The sum content of cobalt, zirconium and manganese was limited to 2.1% by weight, since excess amounts of these elements have no additional positive properties, but rather the processing of the melt is hindered, for example by the mentioned demixing phenomena.
    Preferably, the proportion of cobalt is selected from a range having a lower limit of 0.05% by weight and an upper limit of 1.5% by weight and / or the proportion of manganese selected from a lower limit of 0.1 wt .-% and an upper limit of 0.4 wt .-% and / or the sum of the elements cobalt, zirconium and manganese selected from a range with a lower limit of 0.02 wt .-% and a upper limit of 1.8% by weight.
    Titanium may be contained in an amount selected from a range having a lower limit of 0.05% by weight and an upper limit of 0.5% by weight and / or magnesium in a proportion selected from one Range with a lower limit of 0.01 wt .-% and an upper limit of 0.2 wt .-% wherein the sum content of the elements titanium and magnesium may be selected from a range with a lower limit of 0.05 wt. % and an upper limit of 0.5% by weight.
    These elements are alloyed only in small amounts in order to simplify the melt-metallurgical treatment, in particular with regard to the contamination of the melt with oxides of these metals and the burning of the melt. About the titanium content can be caused different outsourcing processes. At low levels, there is a continuous excretion, at higher levels arise discontinuous excretions. The proportion of titanium is limited to at most 0.5% by weight in order to avoid reverse block segregations (formation of Ti concentration gradients) and thus the setting of uneven properties in the casting. N2011 / 20600 -16- * ·· ** ·· * '·· * ··. ·' .. ·.: .. ♦ · ψ · »·
    The content of magnesium is limited to a maximum of 0.2% by weight so as not to deteriorate the shape changing ability of the tin bronze.
    The sum of titanium and magnesium is limited to a maximum of 0.6 wt .-%, so that the tin bronze is not too hard and the formability suffers.
    Preferably, the proportion of titanium is selected from a range with a lower limit of 0.1 wt .-% and an upper limit of 0.2 wt .-% and / or the proportion of magnesium selected from a range with a lower limit of 0.05% by weight and an upper limit of 0.14% by weight and / or the sum content of the elements titanium and magnesium selected from a range with a lower limit of 0.1% by weight and an upper limit of 0.4% by weight.
    Niobium may be contained in a proportion selected from a range having a lower limit of 0.01% by weight and an upper limit of 0.5% by weight and / or vanadium in a proportion selected from a range having a lower limit of 0.01% by weight and an upper limit of 0.25% by weight and / or iron in a proportion selected from a range having a lower limit of 0.1% by weight. -% and an upper limit of 2.0 wt .-%, wherein the sum of the elements niobium, vanadium, iron may be selected from a range with a lower limit of 0.01 wt .-% and an upper limit of 2 , 0% by weight. For niobium and vanadium, both of which have a fineness of grain, the upper limits were chosen in view of the fact that higher proportions no longer had an additional effect or the additional effect was not achieved to the extent that the addition in a proportion from the claimed ranges.
    The proportion of iron is limited to a maximum of 2% by weight, since at higher levels of zinc, the formability of the tin bronze negative impact iron-zinc phases can form, whereby the tin bronze embrittles.
    For this reason, the sum content of these elements is limited to a maximum of 2 wt .-%, since the negative influence of higher proportions of eggs by the simultaneous presence of niobium and N2011 / 20600-17- ». * * * * Sen / or vanadium.
    However, it has been observed that by the presence of phosphorus in the tin bronze iron can also be grain-fine by the formation of phosphides, which in turn form again crystallization nuclei.
    Preferably, the proportion of niobium is selected from a range having a lower limit of 0.1 wt.% And an upper limit of 0.30 wt.% And / or the proportion of vanadium selected from a lower limit of 0.05 wt% and an upper limit of 0.16 wt% and / or the amount of iron selected from a range having a lower limit of 0.5 wt% and an upper limit of 1.3 % By weight and / or the sum content of the elements titanium and magnesium selected from a range with a lower limit of 0.1% by weight and an upper limit of 1.5% by weight.
    Chromium may be contained in a proportion selected from a range having a lower limit of 0.01% by weight, especially 0.1% by weight, and an upper limit of 1.6% by weight, especially 1.2% by weight.
    The upper limit of at most 1.6% by weight was chosen in view of the possible formation of chromium oxides in the melt, which, like titanium or magnesium, negatively influence the melt metallurgical production by contamination of the melt and the burning off of the melt.
    The proportion of scandium can amount to a maximum of 0.3% by weight, since scandium also has a fine grain, and a higher proportion shows no additional effect.
    The content of boron may be selected from a range having a lower limit of 0.08 wt% and an upper limit of 0.15 wt%, that of carbon from a range having a lower limit of 0.05 wt .-% and an upper limit of 0.15 wt .-%. Since these elements, as has already been stated above, are added to enhance the grain-refining effect of the elements mentioned, higher proportions of these elements have no additional effect, taking into account the proportions of the elements whose grain-refining effect is enhanced.
    The proportion of boron is preferably selected from a range with a lower limit of 0.1% by weight and an upper limit of 0.12% by weight and / or the proportion of carbon selected from a range with a lower limit of 0.07 wt% and an upper limit of 0.12 wt%.
    A portion of the copper can be replaced by nickel in a proportion of not more than 2% by weight, in particular not more than 1.5% by weight, since, as in the case of iron, phosphides can form which act as crystallization nuclei and therefore have a fine grain. This is especially true when the proportion of phosphorus is at most 0.25% by weight.
    In the preferred embodiment of the multilayer bearing shell, however, the bronze is nickel-free and / or aluminum-free. Interestingly, fretting experiments have shown that especially higher nickel additions (which would be necessary for a significant increase in strength, eg over 2 wt.%, As occur in the prior art spinodal-hardening copper-nickel-tin alloys occurrences) are very strong negatively affect the fretting properties. With regard to aluminum, experiments have shown that even small amounts in the tin bronze lead to increased burnup in the production of bronze by the molten metal.
    Although the comments on the composition of the tin bronze for the Gleitla ger gerschicht 2 relate to the preferred embodiment of the invention, other compositions are possible. For example, the bronze-base alloy may contain up to 15% by weight, in particular between 0.5% by weight and 8% by weight, aluminum, up to 10% by weight, in particular between 0.1% by weight and 7.5% by weight, iron, up to 8% by weight, in particular between 0.2% by weight and 7% by weight, nickel, up to 5% by weight, in particular between 0.5% by weight .-% and 3.1 wt .-%, manganese and up to 5 wt .-%, in particular between 0.5 wt .-% and 3.5 wt .-%, silicon or combinations thereof. N2011 / 20600
    Especially with aluminum bronzes, the addition of small amounts of chromium, titanium, zirconium, selenium and tellurium leads to a microstructural refinement and increase of heat resistance. At least one of these elements can therefore be alloyed, with a maximum proportion of these elements being at most 5% by weight. In the event that the plain bearing layer 2 is formed from the at least two sub-layers 3, 4, the sub-layers 3, 4 can be selected from the ranges mentioned above, wherein, however, the second sub-layer 4 is softer than the first sub-layer 3. Es For this reason, consideration must be given to the composition of the bronze-based alloy for the second, inner partial layer 4. For example, the proportion of tin and / or zinc in the second partial layer 4 may be higher than the corresponding proportion in the first partial layer 3 ,
    In the context of test trials of possible, exemplary compositions for the single-layered embodiment of the plain bearing layer 2, the following alloys summarized in Table 1 were prepared. All data are in wt .-%. The remainder forms in each case Cu.
    Table 1: possible composition of the tin bronze
    No. Sn Zn P Co Zr Mn Ti Mg B Nb V Fe Cr Sc C Ni 1 4 1 0.12 "0.05 2 4 1 0.12 0.05 '0.05 3 4 1 0.12 0.05 4 4 1 0,10 0,02 0,05 0,03 5 4 1 0,10 '0,05 "'" "" 0,05 "" "6 4 1 0,05 '0,03' 0, 05 '' '0.1 • 7 4 1 0.10 " "0.05" "*" 0.2 "" 8 4 1 0.01 '0.1 0.05 "" N2011 / 20600 -20- * * * * g 4 1 0.10 0.1 " "" "0.1 " "0.15" "10 4 1 0.12 0.05 '0.05 0.15 0.10 11 5 1 0.12' 0.05 12 5 1 0.12 0.05 '0.05 '' '' '' '' 13 5 1 0,12 0,05 '' '' '' '' '14 5 1 0,10' 0,02 '0,05 0,03' '' '' '15 5 1 0,10 '' 0,05 '' '' '' 0,05 16 5 1 0,05 0,03 0,05 0,1 17 5 1 0,10 '' 0,05 '' '' 0 , 2 18 5 1 0.01 '' '' 0.1 0.05 '19 5 1 0.10 0.1' '' '0.1' '0.15' '' '20 5 1 0.12 0.05 '0.05' '' '' 0.15 '' 0.10 21 8 1 0.12 0.05 "0.05" "*" "" "" * 22 8 1 0,10 '' 0,05 '' '' '0,05' '23 8 1 0,05 0,03 0,05 0,1 24 8 1 0,12 0,05' 0,05 0.15 0.10 25 8 1 0.10 " &Quot; 0.05 "0.2 26 8 5 0.12 0.05 '0.05 27 8 5 0.10" " 0.05 '' '' '0.05' '28 8 5 0.05' 0.03 '0.05' 0.1 '29 8 5 0.12 0.05 0.05 0.15 0.10 30 8 5 0,10 0,05 0,2 N2011 / 20600 -21 - • *
    The plain bearing layer 2 is preferably produced by (horizontal) continuous casting as strip-shaped starting material, which is then rolled off. A fracture separation is preferably not.
    After preparing the Vormateriais for the Gteitlagerschicht 2 or after forming the Vormaterials to form the half, third or quarter shell or socket, the hardness of the bronze base alloy is at least partially reduced by a heat treatment, so in the radial direction of the sliding bearing element 1 as indicated by arrow. 8 a hardness gradient with increasing hardness in the direction of the back 7 of Gleitiagerelementes 1 is formed.
    There are shown in FIGS. 2 to 6 different examples, which are not to be understood as limiting. It should be further noted that these figures are merely simplified representations of the principle of the invention.
    2 to 3 each show a plan view of the sliding surface 6 of the sliding bearing element 1. As can be seen from these figures, areas 9 (or sections) can be formed on the sliding surface 6. These regions have the form of circles (FIG. 2 a), wherein a plurality of such discrete regions 9 can be formed distributed over the sliding surface 6, for example circles arranged in rows, as illustrated in FIG. 2. The rows can also, unlike in Fig. 2, offset from one another (Fig. 2b for the formation in the form of rectangles), for example, every other row by half a distance between the centers of successive circles of a row. The rows are aligned parallel or at least approximately parallel to a longitudinal side edge 10 of the sliding bearing element 1. The longitudinal side edge 10 extends in the circumferential direction of the sliding bearing element. Zigzag arrangements of discrete areas 9 are also possible (FIG. 2c).
    Instead of circles, it is also possible to form other geometric shapes, for example oval regions 9, in particular with a longitudinal extent in the direction of the longitudinal side edge 10, or squares, rectangles, diamonds (FIG. 2d) etc. N2011 / 20600 -22
    It should be noted that the number of areas 9 shown in FIGS. 2 to 3 is not restrictive.
    According to the invention, the regions 9 have a lower hardness than a non-heat-treated region 11 (or section) of the bronze-based alloy following this.
    The regions 9 extend in the radial direction according to arrow 8 (FIG. 1) in the direction of the rear side 7 (FIG. 1) of the sliding bearing element 1. The regions 9 or the region 9 are or is therefore formed in three dimensions.
    3, the region 9 are strip-shaped, wherein in the direction of the longitudinal side edge 10, ie in the circumferential direction of the sliding bearing element 1 a plurality of strip-shaped regions 9 can be formed one behind the other. The areas 9 run obliquely to the longitudinal side edge 10. Both an angle 12, the strips can take to the longitudinal side edge 10, so also a strip width 13 can be variably adapted to the respective application area of the sliding bearing element 1. For example, the angle θ may be selected from a range of 5 ° to a maximum angle calculated from the formula tan'1 ({L / 2) / B), where the parameter L in millimeters is the length of the slide bearing member 1 in the circumferential direction and the parameter B in millimeters describe the width of the sliding bearing element 1. The strip width 13 can be selected from a range of 0.5 mm to a maximum width B, the parameter B in millimeters describing the width of the Gleitiagerelementes 1.
    It is also possible that further strip-shaped regions 9 are formed, which also extend obliquely to the longitudinal side edge 10, but with a different angle, so that the strip-shaped region 9 intersect, as shown in Fig. 3 by dashed lines. The angle that these strips form with the longitudinal side edge 10 can assume the same absolute value or a value different therefrom.
    It is also possible to combine strip-shaped regions 9 with circular regions 9, wherein it should be pointed out that it is generally possible to combine N2011 / 20600 different geometrical shapes of the regions 9 on a sliding surface 6 with one another.
    4 to 6 each show a sliding bearing element 1 in the direction of a longitudinal side surface 14, which is aligned in the circumferential direction of the sliding bearing element 1. To simplify the illustration, the plain bearing elements 1 are shown planar. Of course, these are converted in the finished state to the corresponding partial shell or socket. It should also be clarified with this representation that it is possible within the scope of the invention to form the region 9 with relatively lower hardness prior to forming. It should be noted, however, that the deformation can also take place before the heat treatment to form the regions 9.
    The embodiment of FIG. 4 is designed in the manner of a groove bearing and has a plurality of circumferentially successively arranged strip-shaped regions 9.
    It should be noted at this Stiff that despite the formation of the areas 9, the sliding surface 6 in all embodiments preferably no recessed or raised areas, although this is possible in principle. For example, therefore, the grooved embodiment variant no grooves in the strict sense, since these "grooves" are "filled" with the bronze-base alloy.
    The strip-shaped regions 9 in the embodiment according to FIG. 4 extend perpendicular to the longitudinal side surface 14, that is to say in the axial direction of the plain bearing element 1.
    In principle, it is also possible that only one or two such strip-shaped regions 9 according to FIG. 4 are formed, in which case these regions 9 are preferably subsequently formed on end faces 15 and / or 16. The end faces 15, 16 run perpendicular to the longitudinal side surface 14.
    In the embodiment of the slide bearing element 1 according to FIG. 5, only a region 9 of reduced hardness is formed, which, however, extends over the entire length of time. The length of the surface is N2011 / 20600. · * · * «T«
    ···· * · * »I X
    Gieitfläche 6 of the sliding bearing element 1 extends. The region 9 has a layer depth 17 in the radial direction according to arrow 8 (FIG. 1). This layer depth varies over the course in the direction of the longitudinal side surface 14, ie from the end face 15 to the end face 16, wherein the largest layer depths are formed on the two end faces 15, 16, so that the region 9 at the bottom, the Gieitfläche 6 in Radial direction opposite, has a curved course in the direction of the longitudinal side surface 14. Preferably, the layer depths 17 at the two end faces 15, 16 are the same size and the area 9 is formed symmetrically.
    But it is also possible, as shown in broken lines in Fig. 5, that the arcuate underside extends into the Gieitfläche 6, whereby two discrete areas 9 are formed with a curved bottom, of which one on each of the end faces 15, 16 is arranged.
    According to an embodiment variant, it can be provided that the two regions 9 are formed in the region of the longitudinal side surfaces 14 with a greater depth than a central region of the Gieitfläche 6. This embodiment thus corresponds substantially to that of FIG. 5, but the course of Areas 9 is rotated by 900.
    Finally, it should also be shown with FIG. 6 that in the simplest case it is also possible for the region 9 to extend over the whole surface over the entire casting surface 6, whereby its underside is however formed parallel to the casting surface 6, ie the region 9 has over the entire surface at least approximately the same layer depth 17.
    As already stated above, the region (s) 9 are produced by heat treatment of the bronze-based alloy in discrete regions or over the entire surface, whereby the hardness of the bronze-based alloy in these regions 9 is reduced and a hardness gradient in the radial direction according to arrow 8 (FIG 1) of the sliding bearing element 1 is formed, wherein the hardness increases starting from the Gieitfläche 6 in the direction of the back 7 of the sliding bearing element 1. Thus, in the preferred embodiment of sliding bearing element 1, N2011 / 20600 -25- "** '**' **" * * "* sliding bearing layer 2 consists of a single bronze-base alloy having different hardnesses.
    The heat treatment can generally be done with any suitable device. However, the heat treatment is preferably carried out by means of a laser or by induction heating, since in particular the discrete regions 9 can be manufactured more precisely and simply.
    The heat treatment may be performed in a heat treatment apparatus including or consisting of the laser or the induction heating means, wherein the laser or the induction heating means sweeps the surface of the bronze base alloy during the heat treatment at a speed selected from a range of 1 m / min to 8 m / min, in particular swept at a speed which is selected from a range of 1 m / min to 4 m / min. Depending on this speed and in conjunction with the energy which is introduced into the bronze base alloy in the areas 9 and in the area 9, the layer depth 17 of the area (s) 9 can thus be defined. With these parameters, the grain size of the bronze-based alloy in or in the areas) 9 can be set.
    The laser treatment can be carried out, for example, with a right-handed laser focus selected from a range of 0.5 mm × 10 mm to 0.54 mm × 20 mm or even with a circular laser focus selected from a diameter range of 0.5 mm to 20 mm.
    The power density of the laser treatment can be selected from a range of 0.1 kW / mm 2 to 0.8 kW / mm 2, in particular from a range of 0.2 kW / mm 2 to 0.4 kW / mm 2.
    The power for the induction heat treatment may be selected from a range of 5 kW to 35 kW with a frequency ranging from 10 kHz to 750 kHz. N2011 / 20600 • * '- • 26 · - ·
    In particular, the regions 9 or the regions 9 have a layer depth 17 in the radial direction, which is selected from a region with a lower limit of 0.25 mm to 5 mm, in particular selected from a range of 0.5 mm to 3 mm.
    Generally, this layer depth 17 can be between 1% and 75%, in particular between 5% and 35%, of the plain bearing thickness in the radial direction.
    According to one embodiment variant of the method, it can be provided that at least in a region close to the surface, which may be between 2% and 100% of the layer depth 17, an additional alloying element or even element compounds is introduced into the bronze-based alloy during the heat treatment. For this purpose, this at least one additional alloying element or an additional element compound, for example, wire-shaped or powdered, the area to be treated 9 are supplied. If several areas 9 are formed, it is also possible for only one or only one of these areas 9 to be provided with the additional alloying element.
    As an additional alloying element, for example, the tribologically active elements bismuth, lead and carbon can be used. For example, the tribologically active compounds based on the aluminum oxides (eg Al 2 O 3), silicon carbides (eg SiC) or molybdenum sulphides (eg M0S 2) can be used as additional elemental compound. It is thus possible to alloy the partial layer 4 of the homogeneous plain bearing layer 2 into a heterogeneous microstructure state convert. Similar to the lead in lead or tin in aluminum tin bearing materials, said elements or element compounds serve as a solid lubricant and thereby increase the sliding property of the sub-layer 4 in the case of mixed friction.
    For better adaptation of the sliding bearing element 1 to the intended use can be provided according to another variant of the method that the sliding bearing load is simulated on an electronic data processing system that while the pressure distribution is determined and that thereafter the hardness gradient is adapted to the pressure distribution. Computer programs N2011 / 20600 • · ♦ · · «· > And simulation algorithms for simulating the sliding bearing load are known from the prior art. *** "" * ········································································. For example, hydrodynamic (HD) and / or elastic-hydrodynamic (EHD) calculation methods can be used for this purpose.
    The heat treatment achieves a structural change in the area (s) 9, resulting in a reduction in hardness compared to the base hardness of the bronze-based alloy. In particular, a rolled structure is converted into a cast structure.
    By the heat treatment, the grain size of the grains of the bronze-based alloy can be changed. Tests have shown that the maximum grain size of the non-heat treated areas 11 (or sections) should not exceed a value of 30 pm, in particular 20 pm. The heat-treated area (s) 9 preferably has a particle size of not more than 1000 μm, in particular not more than 300 μm.
    In addition, to achieve the preferred grain size of the non-heat treated regions 11 (or sections), the microstructure having the maximum mean grain size of 30 microns mentioned in the previous section can also be achieved by the addition of fine grain as described above.
    It should be noted at this point that instead of the heat treatment, it is also possible for the sliding bearing element 1, i. its plain bearing layer 2, to be made of at least two different bronze-base alloys, which have a different hardness to each other, wherein the softer bronze-base alloy is disposed in the regions 9. Preferably, however, the sliding bearing layer is made of only a single bronze-base alloy, which is subjected to a heat treatment, as stated above.
    Alternatively or in addition to the process guides mentioned in the preceding paragraphs, a subsequent mechanical or a material-removing machining can also be carried out. Possible processing methods include methods known in the art, e.g. Grinding or fine turning the surface. N2011 / 20600 • - * 28 ·· * * »• *» ·
    The backing metal layer according to the invention can be used in particular for the production of sliding bearing elements 1 in marine diesel engines, in so-called high-speed rotors, in engines for trucks, in high-pressure compressors or in bearing points of wind turbines.
    Figures 7 to 9 show three different hardness profiles, i. Hardness gradients achieved by heat treatment in regions 9 (e.g., Fig. 6). The bronze-based alloy had a composition of 5% by weight of tin, 1.5% by weight of zinc, 0.5% by weight of total trace elements consisting of phosphorus, manganese, nickel, cobalt, titanium and the balance copper.
    The heat treatment was carried out by means of a laser. The power density was 0.3 kW / mm2 in all three experiments. The laser focus was 1mm x 10mm.
    The hardness gradient of Fig. 7 was measured at a speed of treatment, i. 1 m / min, that of FIG. 8 at a treatment speed of 2 m / min and that of FIG. 9 at a treatment speed of 4 m / min formed at a speed with the laser over the surface to be treated.
    In the diagrams, the white areas on the left show the depth to which the bronze base alloy was reflowed by the heat treatment, but the subsequent light gray areas did not melt the depth to which the bronze base alloy was affected by the heat treatment , and the subsequent dark gray area that depth measured from the sliding surface 6, starting from the bronze base alloy unchanged in the original form, ie exists with the original structure.
    It can be seen from the comparison of the hardness profiles that the heat-affected areas, ie the light gray areas, become smaller with increasing treatment speed, ie the layer depth 17 (for example FIG. As a result, so that the hardness gradient can be formed steeper running. In addition, it also allows the hardness of the areas 9 on the N2011 / 20600
    Sliding surface 6 itself be varied, namely, namely, with a higher treatment rate, the hardness decrease is lower, so the surface of the treated areas 9 is even harder.
    To better illustrate these effects, three hardness curves of another embodiment are shown in FIG.
    In general, the bronze-based alloy in the non-heat-treated regions 11 (eg FIG. 2), a Vickers hardness between 160 HV 0.1 and 240 HV 0.1, in particular between 170 HV 0.1 and 200 HV 0.1, exhibit.
    The hardness of the heat-treated regions 9 may be between 80 HV 0.1 and 110 HV 0.1, in particular between 90 HV 0.1 and 100 HV 0.1, on the surface, that is to say on the sliding surface 6 (FIG. 1).
    The hardness gradient can be between 35 HV 0.1 / mm layer depth 17 and 190 HV 0.1 / mm layer depth 17, in particular between 45 HV 0.1 / mm layer depth 17 and 110 HV 0.1 / mm layer depth 17.
    These hardness values are also applicable to the embodiment of the sliding bearing element 1 with a plain bearing layer 2 formed from two partial layers 3, 4.
    The embodiments show possible embodiments of the sliding bearing element 1, wherein it should be noted at this point that various combinations of the individual embodiments are possible with each other and this variation possibility due to the teaching of technical action by objective invention in the skill of those working in this technical field.
    For the sake of order, it should finally be pointed out that, for a better understanding of the construction of slide bearing element 1, these or their components have been shown partly unevenly and / or enlarged and / or reduced in size. N2011 / 20600 * * 4 «* * *« 9 * ** »* *«
    REFERENCE NUMBERS
    Sliding bearing element Sliding bearing layer Partial layer Partial layer Run-in layer Sliding surface Back arrow Area Longitudinal edge Area Angle Strip width Longitudinal side face End face Layer depth N2011 / 20600
    权利要求:
    Claims (15)
    [1]
    A method for producing a sliding bearing element (1) with a support metal forming a bearing back side, and a bearing metal, wherein the support metal is formed from a bronze-based alloy, characterized in that the bearing metal is also made of a bronze-based alloy, and that the hardness of this bronze-based alloy is at least partially reduced by a heat treatment, so that in the radial direction of the sliding bearing a hardness gradient with increasing hardness in the direction of the back (7) of the sliding bearing element (1) is formed.
    [2]
    2. The method according to claim 1, characterized in that the carrier metal and the bearing metal are formed in a single layer and made of a single bronze-based alloy.
    [3]
    3. The method according to claim 1 or 2, characterized in that the heat treatment is carried out by means of a laser or by induction heating.
    [4]
    4. The method according to any one of claims t to 3, characterized in that at least in a near-surface region (9) during the heat treatment, an additional alloying element is introduced into the bronze-base alloy.
    [5]
    5. The method according to any one of claims 1 to 4, characterized in that the heat treatment is carried out with a heat treatment device which during the heat treatment, the surface of the bronze-based alloy at a speed swept, which is selected from a range of 1 m / min 8 m / min.
    [6]
    6. The method according to any one of claims 1 to 5, characterized in that the plain bearing load is simulated on an electronic Datenverarbeitungsan- N2011 / 20600 • «cl -2 days that while the pressure distribution is determined and then formed the hardness gradient adapted to the pressure distribution becomes.
    [7]
    7. plain bearing element (1) with a support metal, which forms a back (7) of the sliding bearing element (1), and a bearing metal, wherein the support metal is formed from a bronze-based alloy, characterized in that the bearing metal is also made of a bronze-based alloy is formed, and that this bronze-base alloy has a hardness gradient with increasing hardness towards the back (7) of the sliding bearing element (1).
    [8]
    8. plain bearing element (1) according to claim 7, characterized in that the carrier metal and the bearing metal are formed in a single layer and formed by a single bronze-based alloy.
    [9]
    9. sliding bearing element (1) according to claim 7 or 8, characterized in that on one of the rear side (7) in the direction of a radial bearing cross-section opposite sliding surface (6) of the bronze-base alloy an inlet layer (5) or a Gleitlackschicht is arranged.
    [10]
    10. sliding bearing element (1) according to one of claims 7 to 9, characterized in that the hardness gradient is formed into a layer depth (17) which is selected from a range of 0.5 mm to 5 mm.
    [11]
    11. plain bearing element (1) according to one of claims 7 to 10, characterized in that the hardness gradient in the region of longitudinal side surfaces (14) of the sliding bearing layer (2) with a greater layer depth (17) is formed as in a central region.
    [12]
    12. plain bearing element (1) according to one of claims 7 to 11, characterized in that the hardness gradient is formed only in discrete areas (9).
    [13]
    13. plain bearing element (1) according to claim 11, characterized in that the discrete regions (9) are formed in the form of strips. N2011 / 20600
    [14]
    The sliding bearing element (1) according to any one of claims 7 to 13, characterized in that the bronze-base alloy has a heat-treated portion (9) and in the at least one heat-treated portion (9) except for the at least one heat-treated portion (9). 9) has a cast structure.
    [15]
    15. plain bearing element (1) according to claim 14, characterized in that bronze-base alloy in the at least one heat-treated region (9) has a grain size of at most 1000 pm. Miba Gleitlager GmbH

    LawyersBlyfger & Partner Attorney at Law N2011 / 20600
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    法律状态:
    优先权:
    申请号 | 申请日 | 专利标题
    ATA60/2012A|AT511432B1|2012-01-20|2012-01-20|METHOD FOR PRODUCING A SLIDING BEARING ELEMENT|ATA60/2012A| AT511432B1|2012-01-20|2012-01-20|METHOD FOR PRODUCING A SLIDING BEARING ELEMENT|
    US13/495,068| US8845199B2|2012-01-20|2012-06-13|Solid bronze bearing with hardness gradient|
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