WO2017127858A1 - Procédé de fabrication d'un élément de palier lisse - Google Patents

Procédé de fabrication d'un élément de palier lisse Download PDF

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Publication number
WO2017127858A1
WO2017127858A1 PCT/AT2017/060011 AT2017060011W WO2017127858A1 WO 2017127858 A1 WO2017127858 A1 WO 2017127858A1 AT 2017060011 W AT2017060011 W AT 2017060011W WO 2017127858 A1 WO2017127858 A1 WO 2017127858A1
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Prior art keywords
copper
layer
precipitates
based alloy
alloy
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PCT/AT2017/060011
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German (de)
English (en)
Inventor
Alexander Eberhard
Lukas HÄDICKE
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Miba Gleitlager Austria GmbH
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Miba Gleitlager Austria GmbH
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C12/00—Solid state diffusion of at least one non-metal element other than silicon and at least one metal element or silicon into metallic material surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C26/00—Coating not provided for in groups C23C2/00 - C23C24/00
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/021—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal alloy layer
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/027—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material including at least one metal matrix material comprising a mixture of at least two metals or metal phases or metal matrix composites, e.g. metal matrix with embedded inorganic hard particles, CERMET, MMC.
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
    • C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
    • C23C28/028—Including graded layers in composition or in physical properties, e.g. density, porosity, grain size
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C6/00—Coating by casting molten material on the substrate
    • 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
    • F16C33/046—Brasses; Bushes; Linings divided or split, e.g. half-bearings or rolled sleeves
    • 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
    • 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
    • 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
    • F16C33/122—Multilayer structures of sleeves, washers or liners
    • 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
    • F16C33/122—Multilayer structures of sleeves, washers or liners
    • F16C33/124—Details of overlays
    • 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
    • F16C33/122—Multilayer structures of sleeves, washers or liners
    • F16C33/125—Details of bearing layers, i.e. the lining
    • 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
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/10—Alloys based on copper
    • 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
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
    • F16C2240/48—Particle sizes
    • 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
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/40—Linear dimensions, e.g. length, radius, thickness, gap
    • F16C2240/60—Thickness, e.g. thickness of coatings
    • 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
    • F16C2240/00—Specified values or numerical ranges of parameters; Relations between them
    • F16C2240/90—Surface areas
    • 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
    • F16C2360/00—Engines or pumps
    • F16C2360/22—Internal combustion engines

Definitions

  • the invention relates to a method for producing a sliding bearing element according to which a composite material of a first layer and one or more further layer (s) is produced, wherein the further layer or one of the further layers is formed as a sliding layer, and as a sliding layer of a casting alloy of a lead-free copper-base alloy is prepared, wherein in the copper-based alloy precipitates are introduced, which have at least one alloying constituent of the copper-based alloy.
  • the invention relates to a sliding bearing member made of a composite material comprising a supporting metal layer and a sliding layer and optionally an intermediate layer between the supporting metal layer and the sliding layer, wherein the sliding layer is formed of a casting alloy of a lead-free copper-base alloy, in the precipitates having at least one alloying constituent of the copper-based alloy , are included.
  • Lead bronzes have long been used in slide bearings for the engine industry because they have a good-natured tribological behavior through the lead precipitates. In addition, their casting technology production is very robust from the process engineering point of view, since the metallurgical phenomena of micro segregation and the associated voids formation are prevented or compensated by the lead. For environmental reasons, however, leaded bronzes should be avoided.
  • brass or bronze cast alloys using alloying additives such as chromium, manganese, zirconium or aluminum are used to improve the friction properties and, in particular, reduce the tendency to seizure.
  • This object is achieved with the aforementioned method for producing a sliding bearing element, after which the copper-based alloy is thermochemically treated after solidification, wherein the copper-based alloy is brought into contact with at least one oxidizing agent, and the oxidizing agent is diffused into the copper-base alloy, so that at least one alloying component of Copper-based alloy is at least partially oxidized to form precipitates within the copper-base alloy, wherein the precipitates are formed only within a sub-layer of the copper-base alloy.
  • the object is further achieved with the slide bearing element mentioned above, in which the precipitates are formed only within a partial layer of the copper-base alloy.
  • the hardness of the sub-layer decreases compared to the hardness of the starting material, whereby the sub-layer, which is close to the surface of the sliding layer, has a reduced tendency to seize.
  • the precipitates themselves act at least partially as solid lubricant, and can therefore replace the lead of lead-containing bronzes. Nevertheless, they prevent crack propagation, as a result of which the microstructure in the partial layer of the sliding layer becomes more viscous.
  • the casting itself can be improved since the alloy system can be made simpler without precipitation particles added in advance.
  • the oxidation is carried out with an oxidizing agent which is selected from a group comprising or consisting of oxygen and oxygen-donating compounds.
  • an oxidizing agent which is selected from a group comprising or consisting of oxygen and oxygen-donating compounds.
  • oxygen or oxygen-releasing compounds as oxidizing agent, the process time can be shortened because oxygen diffuses faster due to the small molecule.
  • thermomechanical treatment of the solidified copper-base alloy is carried out before or simultaneously with the thermochemical treatment, whereby the toughness of the copper-base alloy can be improved.
  • this must not be reheated after the thermochemi treatment, if the forming takes place at elevated temperature, whereby the risk of changes in the mechanical properties of the copper-based alloy, for example by recrystallization phenomena, can be reduced.
  • a change in the excretion can be at least largely avoided by a thermo-mechanical treatment of the sliding layer subsequent to the thermochemical treatment.
  • the microstructure of the copper-based alloy can be made more diffusible by the thermomechanical treatment by the formation of more grain boundaries, whereby the thermochemical treatment can be improved.
  • a copper-based alloy which comprises one or more of the elements from a group comprising boron, antimony, aluminum, silicon, vanadium, phosphorus, titanium, manganese, tin, zinc, magnesium.
  • these elements i. their oxides, in comparison to copper oxides on a much more negative free enthalpy, whereby the process flow can be simplified insofar as the risk of oxidation of copper during the thermochemi see treatment of the copper-based alloy can be significantly reduced.
  • thermochemical treatment of the copper-based alloy can be carried out prior to the composite formation with the layer of the support metal.
  • This has the advantage that with the composite formation, for example by roll cladding, possibly existing defects are at least partially cured.
  • the layer thickness of the sub-layer can be reduced, whereby the proportion of precipitates per unit volume in the sub-layer can be increased.
  • the duration of the oxidation process can be reduced, since it can be terminated as desired even with a lower proportion of precipitates per unit volume.
  • the thermochemical treatment of the copper-based alloy is performed after composing with the backing metal layer.
  • the layer of layered metal can be poured directly onto the support metal layer or the intermediate layer which may be present, whereby the integration of the method into existing processes in the plain bearing industry is easier. It can thus be achieved a corresponding cost advantage.
  • the at least one oxidizing agent can be used solid and / or gaseous or plasma-shaped.
  • the use of a solid oxidizing agent has the advantage that specifically only at least one volume range of the sliding layer can be oxidized.
  • the use of a plasma-form oxidant has the advantage that the oxidation can take place very rapidly, as a result of which the duration of the process can be shortened.
  • plasma-shaped oxidizing agents it is relatively easy to apply the oxidant to the entire surface with a gaseous oxidizing agent, so that the precipitates can be produced relatively quickly by diffusion in the underlying partial layer.
  • Gaseous (non-plasma) oxidants have the advantage that the concentration of the oxidant in the oxidation atmosphere can be easily adjusted and regulated.
  • thermochemical treatment may be carried out at a temperature selected from a range of 500 ° C. to the solidification temperature of the copper-base alloy.
  • the height of the treatment temperature can influence the particle size of the precipitates, since coagulation of the precipitates can be effected with higher temperatures.
  • the oxidant used in gaseous form is used in the oxidation atmosphere with a partial pressure of at least 1.10 -3 atm and a maximum of 3 atm
  • the particle size can also be influenced by the pressure, but with increasing pressure the precipitations become smaller.
  • a partial pressure of less than 1.10 -3 atm particles which are too small result in an improvement in the tribological properties of the copper-based alloy, but to a lesser extent a stable, firmly adhering oxide layer is formed, which would also adversely affect the tribological properties of the copper-based alloy.
  • the precipitates have a maximum particle size of at most 50 ⁇ m, with the precipitates having a maximum particle size between 0.1 ⁇ m and 20 ⁇ m according to a preferred embodiment. Fine-grained precipitates are therefore preferred, since with the same amount of precipitates in the copper-base alloy a more homogeneous distribution of the precipitates within the sublayer and less tendency to seize the overlay can be achieved. In addition, it has been observed that the self-lubricating properties of the precipitates are improved when the precipitates have a particle size between 0.1 ⁇ and 50 ⁇ .
  • the precipitates have a maximum particle size, which decreases gradually in the direction from the surface of the copper-based alloy on the support metal layer, whereby within the sub-layer, a gradual change, in particular increase, the hardness of the sub-layer can be achieved.
  • the sliding layer can thus be optimized in terms of lubricating properties in the area of the surface.
  • the copper-base alloy can be hardened due to the finer excursions, whereby the loadability of the sliding layer can be improved.
  • the number of precipitates in the direction from the surface of the copper-base alloy to the supporting metal layer gradually decreases. Due to the lower number of precipitates in deeper layer planes of the sliding layer, a smaller decrease in the hardness of the copper-base alloy in these deeper layer planes can be achieved.
  • the layer thickness of the sub-layer of the copper-based alloy is preferably between 10 ⁇ and 1000 ⁇ . Although it can be achieved with a layer thickness of less than 10 ⁇ also improve the tribologi see properties of the copper-based alloy, however, suffer at such low layer thicknesses, the long-term performance characteristics of the sliding layer and thus also those of the sliding bearing element.
  • Figure 1 is a plain bearing element in side view.
  • FIG. 2 is a side view of a detail of the sliding layer of a variant of the sliding bearing element
  • Fig. 4 shows a detail of the sliding layer of another embodiment of the
  • FIG. 6 shows a scanning electron micrograph of the sliding layer according to FIG. 5 in the region of the thermochemically treated partial layer in a larger magnification; 7 shows a light microscope photograph of another sliding layer.
  • a sliding bearing element in particular a radial sliding bearing element, made of a composite material in side view.
  • the sliding bearing element 1 is provided in particular for use in an internal combustion engine or for supporting a shaft.
  • the sliding bearing element 1 has a sliding bearing element body 2.
  • the sliding bearing element body 2 comprises a supporting metal layer 3 and a further layer 4 arranged thereon or consists of the supporting metal layer 3 and the further layer 4 connected thereto.
  • the sliding bearing element body 2 can also have additional layers, for example a bearing metal layer 5, which is arranged between the further layer 4 and the supporting metal layer 3, and / or an inlet layer 6 on the further layer 4. Between at least two of the layers of the plain bearing element 1, at least one diffusion barrier layer and / or at least one bonding layer can also be arranged.
  • the support metal layer 3 is made of a steel, the bearing metal layer 5 of a copper alloy with 5% by weight of tin and the remainder copper, the inlet layer of tin or bismuth or of a synthetic polymer containing at least one additive, the bonding layer made of copper or nickel, may be formed.
  • the half-shell enförmige sliding bearing element 1 forms together with at least one other sliding bearing element 7 - depending on the structural design can also be more than another sliding bearing element 7 be present - a sliding bearing 8.
  • the lower plain bearing element is preferably formed in the installed state by the sliding bearing element 1 according to the invention. But there is also the possibility that at least one of the at least one further sliding bearing elements is formed by the sliding bearing element 1 or the entire sliding bearing 8 from at least two sliding bearing elements 2 according to the invention.
  • the sliding bearing element 1 is designed as a plain bearing bush, as indicated by dashed lines in Fig. 1. In this case, the sliding bearing element 1 at the same time the sliding bearing. 8
  • the layer 4 may form a direct coating, for example a radially inner coating of a connecting-rod eye.
  • a direct coating for example a radially inner coating of a connecting-rod eye.
  • the layer 4 is formed as a sliding layer 9.
  • a first embodiment of this sliding layer 9 is shown in FIG.
  • the sliding layer 9 consists of a casting alloy of a copper-based alloy.
  • the copper base alloy is in particular a bronze.
  • other copper base alloys are also usable for the sliding layer 9, for example brass, red brass, although this is not the preferred embodiment of the invention.
  • the copper-base alloy includes, in addition to copper, one or more of the elements selected from the group consisting of boron, antimony, aluminum, silicon, vanadium, phosphorus, titanium, manganese, tin, zinc, magnesium. Since the primary effects of the individual elements are known in prior art copper base alloys, it is to be referred to in this regard. In the preferred embodiment variant, however, the copper-based alloy contains, in addition to copper, at least tin and optionally at least one of the further elements mentioned above.
  • precipitates 10 are contained in the sliding layer. These precipitates 10 are formed from at least one alloying constituent and have at least one of the constituents of the alloy.
  • the precipitates 10 are monovalent or polyvalent oxides of at least one of the alloying constituents of the copper-base alloy.
  • the valency refers to the respective element involved in the reaction, which is oxidized. There are also mixed oxides possible.
  • the precipitates 10 of the copper-base alloy are not added as such, but the precipitates of at least one alloying ingredient are generated due to an oxidation reaction.
  • oxidation in accordance with the general definition, is understood to mean the release of electrons in the course of a chemical reaction, For example, Mg 0 reacts with oxygen to give MgO with the delivery of two electrons.
  • the sliding layer 9 has a layer thickness 11.
  • the layer thickness 11 is in particular between 0, 1 mm and 1.5 mm.
  • the precipitates 10 are not distributed over the entire layer thickness 11 of the sliding layer 9, but their arrangement or design is limited only to a region within a partial layer 12 of the sliding layer 9.
  • the precipitates 10 are within , in particular exclusively within, this partial layer 12 is arranged. Owing to the chosen procedure, oxides which form on the surface of the sliding layer 9 by the oxidation do not form a firm bond with the copper-base alloy, so that these oxides can flake off or be easily removed.
  • the precipitates 10 are predominantly in the grains of the copper base alloy.
  • “predominantly” is meant that at least a proportion of 60% of the precipitates 10, based on the totality of the precipitates 10, is located in the grains of the copper-based alloy, the remainder being in the grain boundaries.
  • the precipitates are distributed relatively uniformly over the entire volume of the partial layer 12.
  • relatively uniform is meant that the difference in the number of precipitates 10 of each two different volume regions of the sub-layer 12 by not more than 5%, in particular by not more than 3%, from each other, being used as a reference value with 100% is a number of precipitates 10 in a volume range of the sublayer 12, which is calculated from the total number of precipitates 10 in the total volume of the sublayer 12 divided by the number of volume areas that comprise the total volume.
  • FIGS. 2 to 4 each show, if appropriate, separate embodiments of the slide bearing element 1, wherein the same reference numerals or component designations are used for the same parts. In order to avoid unnecessary repetition, reference is made respectively to the detailed description of the entire figures.
  • a hardness gradient of the partial layer 12 and thus in the sliding layer 9 can be set.
  • the number of precipitates 10 in the sub-layer 12 gradually decreases or generally varies in the direction from the surface 13 of the copper-base alloy of the sliding layer 9 to the supporting metal layer 3.
  • the concentration of the precipitates 10 in the partial layer 12 can be between 1% by weight and 25% by weight, in particular between 3% by weight and 20% by weight, preferably between 3% by weight and 15% by weight. %.
  • concentration of the precipitates 10 in the partial layer 12 can be between 1% by weight and 25% by weight, in particular between 3% by weight and 20% by weight, preferably between 3% by weight and 15% by weight. %.
  • concentration of more than 25% by weight there is a risk of brittle fracture due to the increased brittle phase content. If the concentration drops below 1% by weight in the partial layer 12, a slight reduction is still observed with respect to the tendency of the sliding layer 9 to seize, but the reduction in the tendency to eat is at least 1% by weight and above. , in particular at least 3 wt .-%, much better.
  • the proportion of the precipitates 10 in the region of the surface 13 of the sliding layer 9 is between 1% by weight. and 20 wt .-%, in particular between 1 wt .-% and 15 wt .-%, and in the direction of the support metal layer 3 to a value between 0 wt .-% and 3 wt .-%, in particular between 0 wt. -% and 1 wt .-%, decreases.
  • the partial layer 12 is subdivided in the direction of the supporting metal layer 3 into ten subpart layers.
  • the partial layer 12 may have a layer thickness 14 (FIG. 2) which is between 1% and 66%, in particular between 3% and 50%, of the layer thickness 11 of the sliding layer 9.
  • the layer thickness 14 of the partial layer 12 is preferably between 0.1 mm and 1.5 mm, in particular between 150 ⁇ and 500 ⁇ .
  • the precipitates 10 may have a maximum particle size 15 (FIG. 2) of not more than 50 ⁇ , in particular between 0.1 ⁇ and 20 ⁇ .
  • the maximum particle size 15 is between 15 ⁇ and 20 ⁇ .
  • the maximum particle size 15 is understood to mean the largest dimension that a particle has.
  • the particle size 15 of the precipitates 10 it is possible in this case for the particle size 15 of the precipitates 10 to remain substantially constant over the entire volume of the partial layer 10, i. that the maximum particle sizes 15 of the precipitates 10 differ by no more than 15%, in particular not more than 10%.
  • the precipitates 10 it is possible, as shown in FIG. 4, for the precipitates 10 to have a maximum particle size 15 which gradually increases in the direction from the surface 13 of the copper-based alloy to the supporting metal layer 3.
  • the particle size 15 of the precipitates 10 can increase by a value which is selected from a range of 0.1 to 80%, in particular from a range of 0.1 to 70%, based on the particle size 15 of the precipitates 10 in the area of the surface 13.
  • the precipitates 10 can have a maximum particle size 15 which gradually decreases or generally varies in the direction from the surface 13 of the copper-base alloy to the support metal layer 3.
  • the particle size 15 of the precipitate 10 can decrease by a value which is selected from a range of 0.1 to 80%, in particular from a range of 0.1% to 70%, based on the particle size 15 of the precipitates 10 in the area of the surface 13.
  • the habit of the precipitates 10 may be at least approximately spherical, at least approximately ellipsoidal or egg-shaped, bulbous, at least approximately cubic, etc., or completely irregular.
  • the precipitates 10 are at least approximately round or at least approximately ellipsoidal.
  • the precipitate 10 is preferably generated only after the casting of the sliding layer 9 or the copper-based alloy by Oxidati on. The precipitates 10 are therefore not added as such to the starting materials of the copper-based alloy.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • a starting material of at least two layers is produced for the production of the sliding bearing element 1.
  • the metal strip or the metal sheet forms the support metal layer 3.
  • the plain bearing element 1 can also have more than three layers.
  • the copper-based alloy can be cast on the respective uppermost layer of the composite material with the support metal layer or another, in particular two-layer, composite material is produced, which is subsequently bonded to the support metal layer or a composite material comprising the support metal layer, for example by roll-plating ,
  • the casting of the copper-based alloy onto the metal strip or the metal sheet or onto a layer of a composite material can take place, for example, by means of horizontal or vertical strip casting.
  • a copper-based alloy is produced in a first step, for example by means of continuous casting and the solidified copper-based alloy is then connected to at least one of the other layers of the sliding bearing element 1, in particular the support metal layer 3, for example by means of roll cladding.
  • the sliding bearing elements 1 is produced by a centrifugal casting process. In this case, preferably no thermomechanical treatment is carried out.
  • the proportions of metallic and optionally non-metallic components in the starting mixture used for the preparation of the sliding layer 9 are selected according to the information in Table 1, plus the proportions of these components, which are consumed during the Oxidati on to the precipitates 10.
  • the precipitates 10 are produced in the sliding layer 9 from the solidified copper-base alloy. These precipitates 10 are produced from at least one of the components of the copper-based alloy.
  • the copper-based alloy is thermochemically treated, wherein the copper-based alloy is contacted with at least one oxidizing agent, and the oxidizing agent is diffused into the copper-base alloy so that at least one alloying constituent of the copper-base alloy at least partially forms the precipitates within the copper-base alloy is oxidized.
  • At least one element from a group comprising oxygen and oxygen-releasing compounds is preferably used as the oxidizing agent, so that oxides are formed as precipitates. It is also possible to use a mixture of different oxidizing agents or the copper-base alloy can also be treated repeatedly with at least one oxidizing agent, for example in successive process steps, each with an oxidizing agent.
  • the at least one oxidizing agent may be, for example, oxygen, water vapor or ozone.
  • the at least one oxidizing agent is used in gaseous or plasma form.
  • the composite material with the cast copper-base alloy in a, in particular closed on all sides, treatment chamber with the oxidizing agent in Kon- in which the oxidizing agent is introduced into the atmosphere of the treatment chamber.
  • the proportion of the spent oxidizing agent over the time of the treatment can be automatically supplemented by a fresh oxidizing agent in the treatment chamber so that an at least approximately equal partial pressure prevails on the oxidizing agent in the treatment chamber.
  • the partial pressure of the gaseous or plasma oxidant used in the Oxidati onsatmosphotre a partial pressure of at least 1.10 "5 atm and of at most 5 atm, in particular of at least 1.10 " 3 atm and at most 3 atm have.
  • the remaining portion of the Oxidati onsatmosphotre preferably forms an inert gas, such as argon, helium, or nitrogen. But it is also possible that the remaining portion of the oxidation atmosphere is formed by air.
  • the temperature at which this thermochemical treatment is carried out is preferably selected from a range of 500 ° C., in particular 600 ° C., up to the solidification temperature of the respective copper-base alloy.
  • the duration of the thermochemical treatment can be selected from a range of 1 hour to 96 hours, in particular from a range of 3 hours to 48 hours.
  • the production of the precipitates 10 takes place after the composite formation of the copper-base alloy with at least one further layer.
  • the thermochemical treatment of the copper-base alloy it is also possible for the thermochemical treatment of the copper-base alloy to be carried out before the composite formation with at least one further layer of the plain bearing element 1, in which case the same process parameters can be used.
  • the at least one oxidizing agent is used firmly.
  • the oxidizing agent may be applied to at least a part of the surface of the copper-base alloy.
  • the treatment temperature and the duration of treatment can be selected from the ranges mentioned above.
  • an oxide powder or mixtures of various oxide powders may be used. Possible oxide powders are, for example, BaO 2 , KMnO 4 ,
  • thermomechanical treatment of the solidified copper-based alloy before or simultaneously with the thermochemi see treatment thermomechanical treatment of the solidified copper-based alloy is performed.
  • the thermomechanical treatment may be for example a rolling, forming or forming.
  • the temperature of the thermo-mechanical treatment can be selected from a range of 450 ° C to 1000 ° C, especially from a range of 750 ° C to 950 ° C.
  • the duration of the treatment seen thermomechanical can be selected from a range of 3 hours to 25 hours, in particular from a range of 5 hours to 20 hours.
  • thermomechanical treatment of the copper-based alloy Due to the thermomechanical treatment of the copper-based alloy, a more permeable structure can be produced by increasing the fraction of grain boundaries. In addition, this can also increase the toughness of the copper-based alloy.
  • the sliding bearing element 1 is produced from the composite material by optionally forming strips from a plate material and by appropriate shaping, for example into a shark shell mold, and optionally finishing work, such as fine boring, etc. These final processing steps are known to the sliding bearing specialist, so that reference is made to the relevant literature.
  • oxidic precipitates 10 are produced as a result of the thermochemical treatment of the copper-base alloy.
  • Table 2 below shows such precipitates 10 together with the (preferred) proportions of the copper base alloy. Again, they are quantities in wt .-% to understand. Furthermore, the proportions are based on the particular cation of the compounds, since other than the exemplified oxides can be produced. By referring to the respective cation, the quantities are also valid for these oxides not listed in Table 2.
  • the cumulative amount of precipitates 10 in the copper base alloy of the sliding layer 9 can be selected from a range of 1% by weight and 25% by weight, especially from a range of 3% by weight to 20% by weight.
  • the proportions and size of the precipitates 10 can be influenced by the concentration of the oxidant and / or the treatment temperature and / or the duration of the treatment. Furthermore, by varying the concentration of the oxidizing agent and / or the treatment temperature over the duration of the treatment, the abovementioned concentration gradient of the precipitates 10 over the layer thickness 14 of the partial layer 12 of the copper-base alloy can be adjusted. By way of the concentration of the oxidizing agent, the particle size 15 of the precipitates and thus also the gradient in the particle size 15 over the layer thickness 14 of the partial layer 12 of the copper-base alloy can be influenced, as has already been explained above.
  • Example 1 The following are some of the experiments performed.
  • Example 1 The following are some of the experiments performed.
  • Example 1 The following are some of the experiments performed.
  • An alloy containing 96% by weight of copper, 3% by weight of tin and 1% by weight of zinc was poured onto a support metal layer 3 made of a steel 220 mm wide and 4 mm thick by means of strip casting.
  • the preheated steel had a temperature of 1070 ° C and a speed of 6 cm / min.
  • the casting alloy is poured at a temperature of 1170 ° C.
  • the steel is cooled by means of oil cooling from below to 100 ° C and thus the casting alloy solidifies in the composite.
  • This composite was a thickness reduction of min 25% and max. 60% subjected to rolling. Thereafter, this material was thermochemically treated by air at 900 ° C for 24 hours.
  • FIGS. 5 and 6 show the scanning electron micrographs of the copper-based alloy for this purpose. The precipitates 10 are clearly visible as bright "dots" within the sub-layer 12 of the copper-base alloy, the points with dark “core” being oxides on which other oxides have grown.
  • this material was thermochemically treated by air for 12 hours at 950 ° C. This resulted in a partial layer 12 with a layer thickness 14 of approximately 130 ⁇ .
  • the light microscope photograph (FIG. 7) shows the resulting partial layer 12 and the resulting precipitates 10 (tin oxides, zinc oxides and their mixed oxides) as dark "dots".

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • General Engineering & Computer Science (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Composite Materials (AREA)
  • Inorganic Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)

Abstract

L'invention concerne un procédé de fabrication d'un élément de palier lisse (1), procédé selon lequel un matériau composite constitué d'une première couche et d'une ou de plusieurs autres couches est produit. L'autre couche ou l'une des autres couches est réalisée sous la forme d'une couche de glissement (9) et la couche de glissement (9) est obtenue à partir d'un alliage coulé formé par un alliage à base de cuivre sans plomb. Des dépôts (10), qui comportent au moins un constituant de l'alliage à base de cuivre, sont incorporés dans l'alliage à base de cuivre. L'alliage à base de cuivre est traité de manière thermochimique après la solidification. L'alliage à base de cuivre est mis en contact avec au moins un agent oxydant et l'agent oxydant est diffusé dans l'alliage à base de cuivre de telle sorte qu'au moins un constituant de l'alliage à base de cuivre est oxydé au moins partiellement pour former les dépôts (10) dans l'alliage à base de cuivre. Les dépôts (10) ne sont formés que dans une sous-couche (12) de l'alliage à base de cuivre.
PCT/AT2017/060011 2016-01-28 2017-01-27 Procédé de fabrication d'un élément de palier lisse Ceased WO2017127858A1 (fr)

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WO2019144173A1 (fr) * 2018-01-29 2019-08-01 Miba Gleitlager Austria Gmbh Élément de palier lisse multicouche contenant une couche constituée d'un alliage de cuivre contenant de l'étain, du zinc et du soufre
CN111911535A (zh) * 2019-05-07 2020-11-10 米巴滑动轴承奥地利有限公司 多层滑动轴承元件
CN115213638A (zh) * 2022-07-22 2022-10-21 上海涟屹轴承科技有限公司 一种圆锥破碎机用复合铜合金部件及其制造方法

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EP2365109B1 (fr) * 2010-03-02 2013-05-01 KS Gleitlager GmbH Matériau composite de coussinet doté d'une couche de roulement isolée de manière galvanique
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DE102005063324A1 (de) * 2005-05-13 2006-11-16 Federal-Mogul Wiesbaden Gmbh & Co. Kg Gleitlagerverbundwerkstoff, Verwendung und Herstellungsverfahren
DE102014207331A1 (de) * 2014-04-16 2015-10-22 Federal-Mogul Wiesbaden Gmbh Bleifreier CuNi2Si-Gleitlagerwerkstoff unter Zugabe eines spanbrechend wirkenden Metalls

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WO2019144173A1 (fr) * 2018-01-29 2019-08-01 Miba Gleitlager Austria Gmbh Élément de palier lisse multicouche contenant une couche constituée d'un alliage de cuivre contenant de l'étain, du zinc et du soufre
CN111911535A (zh) * 2019-05-07 2020-11-10 米巴滑动轴承奥地利有限公司 多层滑动轴承元件
CN115213638A (zh) * 2022-07-22 2022-10-21 上海涟屹轴承科技有限公司 一种圆锥破碎机用复合铜合金部件及其制造方法

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