WO1998017833A2 - Materiau pour palier lisse compose d'alliage d'aluminium exempt de silicium hormis les impuretes inherentes a l'elaboration de l'acier - Google Patents

Materiau pour palier lisse compose d'alliage d'aluminium exempt de silicium hormis les impuretes inherentes a l'elaboration de l'acier Download PDF

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Publication number
WO1998017833A2
WO1998017833A2 PCT/AT1997/000223 AT9700223W WO9817833A2 WO 1998017833 A2 WO1998017833 A2 WO 1998017833A2 AT 9700223 W AT9700223 W AT 9700223W WO 9817833 A2 WO9817833 A2 WO 9817833A2
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WO
WIPO (PCT)
Prior art keywords
weight
aluminum alloy
layer
aluminum
tin
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Application number
PCT/AT1997/000223
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German (de)
English (en)
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WO1998017833A3 (fr
Inventor
Robert Mergen
Original Assignee
Miba Gleitlager Aktiengesellschaft
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Filing date
Publication date
Application filed by Miba Gleitlager Aktiengesellschaft filed Critical Miba Gleitlager Aktiengesellschaft
Priority to AU46931/97A priority Critical patent/AU4693197A/en
Publication of WO1998017833A2 publication Critical patent/WO1998017833A2/fr
Publication of WO1998017833A3 publication Critical patent/WO1998017833A3/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
    • F16C33/02—Parts of sliding-contact bearings
    • F16C33/04—Brasses; Bushes; Linings
    • F16C33/06—Sliding surface mainly made of metal
    • F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
    • F16C33/121—Use of special materials

Definitions

  • the invention relates to an aluminum alloy according to the preamble of claim 1 and to a composite material formed therefrom according to claim 16 and a method for producing composite materials from an aluminum alloy as described in the preamble of claim 28.
  • silicon-containing aluminum-tin alloys In order to avoid the disadvantages of silicon-containing aluminum-tin alloys when used in plain bearings with regard to a lower fatigue strength due to the notch effect of the silicon particles on the one hand and the cutting effect of the silicon particles in the area of the sliding surface on the other hand, silicon is often not alloyed.
  • silicon-free aluminum alloys with a high tin content of 35% by weight to 65% by weight, it has already been proposed (DE 42 31 862 AI), on the one hand lead and bismuth in a total amount of 0 , 5% by weight to 1.0% by weight and, on the other hand, at least one of the elements manganese, nickel, silver, magnesium, antimony and zinc in a total amount of at most 5% by weight.
  • Aluminum alloys with a high tin content are also known from other documents.
  • DE 40 04 703 A1 discloses a layer material for slide bearing elements with an aluminum-based anti-friction layer. In addition to the usual permissible impurities, this contains additions of 1% by weight to 3% by weight of nickel, 0.5% by weight to 2.5% by weight of manganese and 0.02% by weight to 1.5% by weight Copper.
  • the tin content is intended to be 0.5% to 20% by weight. With this composition it is achieved that in a matrix of AlNiMnCu mixed crystals, in addition to embedded hard particles, there is a tin phase in the form of dispersed tin particles.
  • This tin substitute is intended to achieve largely trouble-free running on the slide bearing element even at higher speeds, reduced friction and improved emergency running properties.
  • the tin additive is to be replaced by a lead additive in the range between 1% by weight and 10% by weight, from which it can be concluded that such an aluminum alloy with the high tin content contained therein can only be used to a limited extent in plain bearings for high-performance engines due to the deficient distribution of the tin phase - can be used.
  • a multilayer plain bearing which comprises an aluminum-tin bearing alloy layer with a tin content of 7 wt.% To 20 wt.%, Is known from DE 43 32 433 AI.
  • tin content exceeds 20% by weight, the mechanical properties of the bearing alloy deteriorate and such a bearing alloy cannot be used under harsh conditions, such as in the case of a high-performance engine. For this reason, it is also planned to add silicon in a proportion of up to 4% by weight.
  • AI is a bearing alloy based on aluminum-tin
  • the fatigue strength is to be improved by reducing the drop in hardness at high temperatures and in particular by avoiding coarsening of the tin particles.
  • the wear resistance of the bearing alloy is to be increased in order to improve the durability compared to a shaft to be supported.
  • the disadvantage here is that in order to maintain these properties, a high proportion of 0.1 to 1% by weight of chromium has to be added to the aluminum alloy in order to maintain the distribution of the tin.
  • intermetallic Al-Cr compounds are formed in a quantity ratio that the use of this aluminum-tin alloy in high-performance engines is only possible to a limited extent.
  • a bearing alloy based on aluminum is known from US 4,471,032 A, to which between 1.5% by weight and 35% by weight tin are added.
  • this alloy contains between 1% by weight and 11% by weight of at least one element from the group consisting of manganese, iron, molybdenum, nickel, zirconium, cobalt, titanium, antimony, niobium and chromium, so that intermetallic hard particles are formed here, too to improve the endurance properties of a slide bearing formed from it under difficult conditions.
  • the proportion of these hard phases in the matrix however, complicates their use in high-performance motors, since the desired lubricating effect of the tin is reduced to a not inconsiderable extent.
  • WO 97/22725 A describes an aluminum alloy which simultaneously has a has high tin content and high strength.
  • the latter is achieved, among other things, by the formation of intermetallic phases that solidify the aluminum matrix.
  • the composition is chosen so that the shape of the hard intermetallic precipitates does not have a negative effect on the matrix strength.
  • the special wetting behavior of these precipitates with the tin contributes to improving the structural strength - because of the minimal disruption of the matrix structure by the tin network.
  • the use of very little aluminum-soluble formers of intermetallic phases has the disadvantage that the possible curing effects are not exploited here or that the achievable curing effect can only be reproduced in fairly wide margins.
  • the invention is therefore based on the object of providing an aluminum alloy whose structural strength and mechanical properties are improved even at higher tin contents.
  • the object of the invention is solved by the features in claim 1. It is advantageous here that the disadvantages and shortcomings of the alloys listed according to the prior art are solved in that in the matrix alloy, in which the content of sparingly soluble aluminide formers is reduced to a minimum, such matrix-reinforcing elements are additionally added, which are in the Aluminum matrix are less soluble. It is thus possible to provide aluminum alloys for layers, in particular plain bearings, which in addition to the required hardness also have a large proportion of tin dispersed in the aluminum matrix.
  • the elements of the group lead, bismuth, antimony and indium can influence the interfacial tension of the tin, the elements of the group magnesium and zinc that of the aluminum and thus overall the wettability of the aluminum matrix by the tin in such a way that it solidifies the aluminum matrix cannot deposit the tin as a coherent network at the grain boundaries of the matrix.
  • the interruption of the mesh structure of the tin phase thus leads to a change in the microstructure and brings about a corresponding increase in the structural strength of the bearing material and an improved formability.
  • the elements that are predominantly soluble in tin or predominantly in aluminum must be added in a quantity dependent on the tin or aluminum content in order to achieve the desired effect.
  • the object of the invention is also achieved by claim 2, according to which it is possible lent is to choose an aluminum alloy in the composition so that, due to the high zinc content and the lack of soft particles, the possibility of producing laminates is decisively improved.
  • the configuration according to claim 3 makes it possible, on the one hand, to avoid known disadvantages of aluminum alloys with a high tin content by forming a coherent tin network, and on the other hand to give these alloys advantageous strength.
  • the advantageous aluminum alloy according to claim 4 makes it possible to use such alloys with a high tin content also in the field of high-performance engines and at the same time to satisfy the desire for ever longer maintenance intervals.
  • Embodiments according to claims 5 and 6 are also advantageous, according to which an aluminum alloy with a high volumetric proportion of soft phases is available, which allows use in motors with rapidly rotating shafts without premature signs of fatigue being observed.
  • the proportion of alloyed elements lies in a weight range which prevents intermetallic phases resulting from connection formation from changing the structure of the alloy in such a way that no damage occurs to those which come into contact with such alloys Parts done.
  • Embodiments according to claims 12 and 13 are also advantageous, since the
  • an embodiment according to claim 14 is also advantageous, since not only an increase in the hardness of the alloy is possible, but also a certain adjustment of the desired hardness.
  • Another advantage is the embodiment according to claim 15, according to which the microstructure can be changed by a controlled measure and can be adapted to the desired properties of the aluminum alloy.
  • the object of the invention is also achieved by the features in claim 16, according to which a composite material, in particular a slide bearing, is now available which is distinguished by the improvements in the material, for example the cold formability, the cold rollability, of the aluminum alloy used.
  • the hardness of the intermediate layer can be adjusted by the specified elements so that it can function as a bonding layer between layers made of an aluminum alloy and, for example, steel, without the composite being destroyed. Is to be feared.
  • an embodiment according to claim 23 is also advantageous since it creates the conditions for a long service life of the composite material. By coordinating the hardness of the individual layers in this way, the cohesion of the composite material can be favorably influenced in favor of the service life.
  • the composite material can also be used in the area of plain bearings, as this ensures a sufficient supply of lubricant as well as a corresponding removal of the frictional heat.
  • An embodiment according to claim 26 is also advantageous, according to which a lateral discharge of undesired solid particles is possible.
  • a composite material can be made available whose alternating load or fatigue strength is advantageously improved in spite of the increased soft phase content in the aluminum alloy.
  • a composite material can be produced from an aluminum alloy, which is distinguished on the one hand by its hardness and on the other hand by its sliding properties, in particular its lubricating properties, so that it can be used for plain bearings.
  • This composite material produced in this way also enables the manufacture of plain bearings for high-performance engines.
  • With a composite material designed in this way it is also possible to significantly extend the maintenance intervals of plain bearings.
  • the difficulties caused by lubricants that have been used for a long time, for example contamination by increased solids content and the associated reduced lubricity, are compensated for by a composite material designed in this way.
  • Embodiments according to claims 29 and 30 are advantageous, since this eliminates the unintentional stresses in the composite material caused by the rolling and the structure of the layers on which the composite material is based are influenced in a favorable manner.
  • FIG. 2 shows an embodiment variant of a slide bearing according to the invention with a three-layer structure
  • Fig. 3 is a diagram showing the fatigue strength of a plain bearing according to the invention.
  • FIG. 1 shows a bearing element 1 of a slide bearing 2, the running layer 3 of which is formed from an aluminum alloy 4 according to the invention.
  • the running layer 3 is covered on a surface 5 by a support layer 6, which is usually formed from a metallic material, such as steel, and a part that is intended to absorb forces transmitted to the running layer 3 by a shaft.
  • the bearing element 1 is designed as a half-shell, but of course variants with full shells can also be formed from the aluminum-based alloy according to the invention, as shown in FIG. 1 with dashed lines.
  • Bearing elements 1 of this type are usually used to support parts which can rotate, for example shafts for machines, motors, etc. Since these shafts are normally operated at high speeds - with the exception of the start-up and shutdown phases - it is necessary to lock the bearings and prevent wave.
  • the running layer 3 as an aluminum alloy with a high tin content, to provide in the running layer 3 a groove 7 which serves to receive and supply a suitable lubricant, for example oil.
  • This groove can either be designed as a flat notch with side walls 9 widening in the direction of an end face 8, or else as a circumferential de groove are attached, as shown in Fig. 1 with the dash-dotted lines.
  • lubricants such as through holes.
  • the running layer 3 is fixed to the support layer 6 by e.g. Plating, rolling, welding, gluing, stapling, etc. connected to ensure a secure load transfer.
  • Plating e.g. Plating, rolling, welding, gluing, stapling, etc. connected to ensure a secure load transfer.
  • the aluminum alloy 4 consists of at least 16% by weight of tin and a total of at most 11% by weight of other elements such as magnesium, zinc, lead, bismuth, lithium, antimony, indium, iron, chromium, manganese, copper, or the like the latter elements can be individually, ie they do not necessarily have to be present in combination in the alloy, but with the restriction that an element from the group of magnesium and zinc and an element from the group of lead and bismuth must be alloyed.
  • the proportion of copper is between 0.65% by weight and 1.80% by weight, preferably between 1.35% by weight and 1.45% by weight, in particular 1.44% by weight, that of manganese between 0.
  • composition is of course only one example of many possible variations, the enumeration of which is impossible here. However, this does not mean that the invention is limited to this example.
  • alloys of this type with the specified limits of elements to be added that after the melting of the components and the subsequent cooling, so-called hard particles are formed, which are formed in the multicomponent system through the formation of compounds, for example aluminide.
  • these hard particles take on the function of the hardness of the alloy, on the other hand, they ensure that the large proportion of tin does not form a coherent tin network, which would disturb the matrix structure and thus the structural strength.
  • the solidification of the aluminum matrix is heavily dependent on the morphology of these intermetallic phases. Since spherodization annealing, as e.g. is used to minimize the friction effect of aluminum alloys with hard silicon particles, because of the expected precipitation and aggregation of the tin with the associated disadvantages, the alloy elements such as e.g. Antimony added to reduce the notch effect of the hard particles.
  • the method according to the invention consists above all in that the special element combination of the matrix alloy, in which the content of sparingly soluble aluminide formers is reduced to a minimum, achieves matrix reinforcement by elements which are less readily soluble in the aluminum matrix .
  • the elements of the group lead, bismuth, antimony and indium can influence the interfacial tension of the tin, through the elements of the group magnesium, zinc and lithium that of aluminum and thus overall the wettability of the aluminum matrix by the tin in such a way that it solidifies the aluminum matrix cannot deposit the tin as a coherent network at the grain boundaries of the matrix.
  • the interruption of the mesh structure of the tin phase thus leads to a change in the microstructure and advantageously to a corresponding increase in the structural strength of the alloy, and thus of the bearing element 1, and to improved formability.
  • the elements which are predominantly soluble in tin or predominantly in aluminum, are dependent on the tin or aluminum content in order to achieve the desired effect.
  • amount to be added which is determined by the maximum solubility of the individual elements at eutectic temperature.
  • the proportion of the respective element from the group of elements that contains antimony and indium in addition to lead and bismuth should be between 10% and 75% of the maximum solubility of the respective element in the total tin content, but the total proportion of this group of elements should be at least 50% and at most 350% of the maximum Solubility of the at least tin-soluble group element.
  • the proportion of the respective element from the element group containing magnesium and zinc as well as lithium should be between 6% and 50% of the maximum solubility of the respective element in the total aluminum content, but the total proportion of this element group should be at least 25% and at most 150% of the maximum solubility of the least soluble group element in aluminum.
  • the specified upper and lower limit values for the proportions of the elements related to the tin or aluminum content represent a sufficient effect on the change in the interfacial tension for the suppression of a coherent network structure of the tin, without having to fear an adverse interaction with the elements of the matrix alloy .
  • an element fraction beyond the maximum solubility may well be reasonable within the limits specified, because these elements already start to work in the gradually solidifying melt.
  • the two alloys to be examined were cast under the same conditions in a horizontal continuous casting in strip form, with a width of 100 mm and a height of 10 mm.
  • the heat dissipation during the solidification process was between 3.4 J / s and 3.7 J / s in both cases due to the chosen draw ratio. Since the highest possible total deformation without interruption due to intermediate annealing in the case of bearing materials made of an aluminum alloy leads to advantageous mechanical and tribological properties, the deformability of the two alloys was investigated.
  • the known plain bearing material was subjected to a heat treatment at 350 ° C. for a period of Subject to 3 hours. This annealing treatment increases the globulization of the tin particles.
  • the alloy according to the invention was examined without heat treatment at a temperature of 350 ° C. over a period of 3 and 19 hours.
  • the cast skin was removed from the samples of both the known and the aluminum alloy according to the invention by milling.
  • the sample cross section was then 80 x 8 mm. The rolling reductions permitted without intermediate annealing were determined with these samples.
  • the Vickers hardness of the aluminum alloy according to the invention could be determined in the cast state after cooling with 42 HV2 in and transversely to the continuous casting direction. After the running layer 3 had been plated onto the steel of the support layer 6 by rolling with 45% puncture and the temperature treatment at 350 ° C. for 3 hours, the hardness could be determined with 52 HV2 in and across the rolling direction. The hardness of the
  • Aluminum alloy should definitely be at least 20% higher than transverse to the casting direction after being plated on steel by rolling and annealing at 300 ° C to 400 ° C for two to five hours, preferably 350 ° C for three hours in and across the direction of rolling in the as-cast state.
  • the hardness should also have a value in and across the rolling direction of 48 HV2 to 68 HV2, preferably 50 HV2 to 54 HV2.
  • the hardness of the steel should be reduced by rolling with at least 40% stitch in at most two passes or with at least have at least 25% stitch in at most one stitch and subsequent annealing at 300 ° C to 400 ° C for two to five hours, preferably 350 ° C for three hours in and across the rolling direction at least 175 HV5.
  • the aluminum alloy according to the invention has the advantageous property of strengthening by forming, in particular by rolling, and is therefore also suitable for use in high-performance engines.
  • the latter can also be justified by the fact that aluminum-based alloys which correspond to the invention have a sufficiently high soft phase content, so that altogether such aluminum matrix alloys have tribological properties which take into account the strong desire for ever longer maintenance intervals.
  • the content of soft phases has the effect that damage to the bearing and shaft due to the lubricant, which is heavily contaminated due to the long maintenance intervals and is loaded with solid particles from the abrasion, is avoided.
  • An advantageous property of the aluminum alloy according to the invention or of the bearing materials formed therefrom is also their post-hardening, e.g. in engines as a result of the temperature load during operation, which, as is known, can only be avoided to a limited extent by the lubricant. In this way it can be permanently avoided that the finely distributed, unbound tin particles flow together to form larger particles due to repeated temperature changes - tin is known to have a melting point of 232 ° C, a temperature that is quickly reached by running waves - and is eliminated.
  • FIG. 2 shows another embodiment variant of a slide bearing 2 according to the invention in a simplified, schematic representation as a half-shell.
  • the composite material for the bearing element 1 additionally comprises an intermediate layer 10, which is arranged between the running layer 3 and the support layer 6.
  • the layers are connected to one another in a non-moving manner by the methods already mentioned.
  • the hard particles 11 already mentioned are also indicated schematically and disproportionately in this figure.
  • the aluminum alloy 4 for the running layer 3 has already been discussed in detail above, so that in the following only the intermediate layer 10 is treated.
  • the support layer 6 is also preferably made of steel, but other metallic materials can also be used.
  • the entire previous versions are of course also applicable to this variant.
  • the intermediate layer 10 can also be formed from an aluminum-based alloy. However, care must be taken to ensure that, in the case of a multilayer composite constructed in this way, it is favorable that the hardness of the individual layers is matched to one another. In the specific case, this means for the composite material according to the invention that the hardness increases in the order of the running layer 3, intermediate layer 10, support layer 6, which ensures firm cohesion of the layers and thus the intermediate layer 10 can take on the function of a bonding layer. The increase is necessary because the running layer 3 consists of the material that has the lowest hardness of a plain bearing.
  • An aluminum-based alloy can also be used as the material for the intermediate layer 10, but with a different composition to the overlay 3, for example an AlZn4.5 alloy.
  • other alloys and metallic materials such as e.g. Pure aluminum with the usual impurities.
  • the properties sought for the bearing element 1 can be decisively influenced by such a coordination of the alloys for the running layer 3 and the intermediate layer 10 with one another.
  • An aluminum alloy is preferably used, which at least one hard material-forming element from the group manganese, iron, cobalt, chromium, zirconium, copper, nickel, platinum, magnesium, antimony, tungsten, niobium, vanadium, molybdenum, lithium or the like
  • the amount of zinc can be up to the maximum solubility in the total amount of aluminum.
  • plain bearings 2 can also be produced in a closed ring shape according to methods corresponding to the prior art. For this purpose, these are cast as a ring in accordance with predefined raw dimensions or formed from a rolled profile or extruded profile into corresponding rings and connected, in particular welded, at the front ends to form an uninterrupted ring.
  • the aforementioned materials and alloys can of course also be used for such plain bearings 2.
  • the fatigue strength shown in FIG. 3 also testifies to the excellent material properties of an aluminum alloy according to the invention.
  • a test piece was made that was constantly bent in a test device.
  • the edge stresses on the steel originally in the plated alloy result as Function of the bending moment and the specimen stiffness.
  • the greatest deflection is achieved in the area of a circular saving on the test specimen. Accordingly, a crack will occur here after a certain number of load changes, which in turn is detected by crack detection strips firmly adhered to the surface.
  • the diagram shows the course of load changes as a function of the applied voltage, with the bending stress in MPa on the abscissa and the number of load changes on the ordinate.
  • the first step is to produce the aluminum alloy with the required additions of specified elements - at least 16% by weight of tin and a maximum of 11% by weight of other elements - in a continuous casting process.
  • the heat is dissipated when the melt cools, in order to achieve the desired structure with 3.4 J / s to 3.7 J / s.
  • At least one further layer is subsequently connected to a first layer made therefrom so as to be non-moving, for example by plating on by rolling.
  • a temperature treatment is carried out at at least 250 ° C., preferably 300 ° C. to 550 ° C.
  • the composite material is subjected to a temperature treatment of a maximum of 450 ° C., preferably 150 ° C. to 375 ° C.
  • Fig. 1; 2; 3 shown embodiments form the subject of independent, inventive solutions.
  • the tasks and solutions according to the invention in this regard can be found in the detailed descriptions of these figures.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)

Abstract

L'invention concerne un alliage d'aluminium (4) pour produire un revêtement, notamment pour un palier lisse (2), qui est exempt de silicium, hormis les impuretés inhérentes à l'élaboration de l'acier, et comprend pour principal élément d'alliage, outre de l'étain, au moins dans chaque cas, un élément d'une part du groupe d'éléments contenant le plomb et le bismuth et d'autre part, du groupe d'éléments contenant le magnésium et le zinc. La quantité minimale d'étain s'élève à 16 % en poids. Tous les autres constituants de l'alliage sont présents dans une quantité ne dépassant pas au plus 11 % en poids. Chacun des éléments du groupe contenant outre le plomb et le bismuth, l'antimoine et l'indium est présent dans une quantité comprise entre 10 et 75 % de la solubilité maximale de chaque élément dans la teneur globale en étain.
PCT/AT1997/000223 1996-10-18 1997-10-17 Materiau pour palier lisse compose d'alliage d'aluminium exempt de silicium hormis les impuretes inherentes a l'elaboration de l'acier WO1998017833A2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AU46931/97A AU4693197A (en) 1996-10-18 1997-10-17 Sliding bearing material made from an aluminium alloy which is silicon-free apart from impurities necessitated by steel production

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Application Number Priority Date Filing Date Title
ATA1827/96 1996-10-18
AT182796 1996-10-18

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WO1998017833A2 true WO1998017833A2 (fr) 1998-04-30
WO1998017833A3 WO1998017833A3 (fr) 1998-08-06

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Cited By (3)

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Publication number Priority date Publication date Assignee Title
US6506503B1 (en) 1998-07-29 2003-01-14 Miba Gleitlager Aktiengesellschaft Friction bearing having an intermediate layer, notably binding layer, made of an alloy on aluminium basis
EP1522750A1 (fr) * 2003-10-06 2005-04-13 Taiho Kogyo Co., Ltd. Palier lisse à plusieurs couches
CN106498211A (zh) * 2016-11-29 2017-03-15 华南理工大学 纳米氧化铝颗粒原位增强高热稳纳米相复合结构Al‑Sn合金的制备方法

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DE4231862A1 (de) * 1991-10-02 1993-04-08 Daido Metal Co Ltd Metall-lager fuer grossmotoren

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6506503B1 (en) 1998-07-29 2003-01-14 Miba Gleitlager Aktiengesellschaft Friction bearing having an intermediate layer, notably binding layer, made of an alloy on aluminium basis
EP1522750A1 (fr) * 2003-10-06 2005-04-13 Taiho Kogyo Co., Ltd. Palier lisse à plusieurs couches
CN106498211A (zh) * 2016-11-29 2017-03-15 华南理工大学 纳米氧化铝颗粒原位增强高热稳纳米相复合结构Al‑Sn合金的制备方法
CN106498211B (zh) * 2016-11-29 2018-06-29 华南理工大学 纳米氧化铝颗粒原位增强高热稳纳米相复合结构Al-Sn合金的制备方法

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