US20160348215A1 - Lubricant-Compatible Copper Alloy - Google Patents

Lubricant-Compatible Copper Alloy Download PDF

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US20160348215A1
US20160348215A1 US15/104,437 US201515104437A US2016348215A1 US 20160348215 A1 US20160348215 A1 US 20160348215A1 US 201515104437 A US201515104437 A US 201515104437A US 2016348215 A1 US2016348215 A1 US 2016348215A1
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copper alloy
alloy
silicon
weight
copper
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Hermann Gummert
Björn Reetz
Thomas Plett
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Otto Fuchs KG
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Otto Fuchs KG
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Assigned to OTTO FUCHS KOMMANDITGESELLSCHAFT reassignment OTTO FUCHS KOMMANDITGESELLSCHAFT ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: Gummert, Hermann, Dr., PLETT, THOMAS, MR., REETZ, BJÖRN, DR.
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/01—Alloys based on copper with aluminium as the next major constituent
    • 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
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/165—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon of zinc or cadmium 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
    • 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
    • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
    • F16D23/00—Details of mechanically-actuated clutches not specific for one distinct type
    • F16D23/02—Arrangements for synchronisation, also for power-operated clutches
    • F16D23/025—Synchro rings
    • 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
    • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
    • F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
    • F16D69/02—Composition of linings ; Methods of manufacturing
    • 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
    • F16H—GEARING
    • F16H57/00—General details of gearing
    • 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
    • F16C2204/00—Metallic materials; Alloys
    • F16C2204/10—Alloys based on copper
    • F16C2204/14—Alloys based on copper with zinc as the next major constituent
    • 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
    • F16C2361/00—Apparatus or articles in engineering in general
    • F16C2361/61—Toothed gear systems, e.g. support of pinion shafts
    • 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
    • F16C33/10—Construction relative to lubrication
    • F16C33/1025—Construction relative to lubrication with liquid, e.g. oil, as lubricant

Definitions

  • the present disclosure relates to a lubricant-compatible copper alloy which is suitable in particular for producing gear components that come in contact with lubricant and are exposed to friction stresses, such as synchronizer rings, as well as a method for manufacturing such gear components and a gear having such gear components.
  • the entire tribological system must be taken into account for the development of a copper alloy for manufacturing workpieces or components, such as synchronizer rings, that are exposed to oil and to friction stresses so that they will have an improved corrosion resistance.
  • the local temperature distribution established in the case of friction stress and the aging behavior of the lubricant have an influence on the wear due to corrosion.
  • an adsorption layer consisting primarily of lubricant additives is formed after only a brief contact time with a lubricant under a frictional load.
  • a reactive layer develops beneath the adsorption layer comprised of components of the adsorption layer and alloy constituents near the surface reacting with one another.
  • the adsorption layer and the reaction layer form an outer boundary layer on the copper alloy workpiece, beneath which there is an internal boundary layer several micrometers thick. Because of the proximity to the outer boundary layer, this internal layer is influenced by the mechanical load acting on the surface as well as by the chemical transformation processes taking place in the reaction layer. Diffusion processes and oxidation processes involving the substrate alloy can also influence the formation of the reaction layer in the region of the internal boundary layer.
  • lubricants contain additives, such as additives that contain sulfur and phosphorus, that can have a corrosive effect under the corresponding thermomechanical load due to friction contact, which in turn causes a not insignificant reduction in the lifetime of the workpiece.
  • Copper alloys have already been proposed for reducing the corrosive effect of sulfur constituents in a lubricant.
  • JP S 60162742 A describes a copper alloy for the bearing of a turbocharger which consists of 57-61% Cu, 2.5-3.5% Pb, based on the amounts by weight, where Fe and Zn may be present as impurities.
  • a stable CuS layer is said to develop on the friction surface.
  • EP 0 872 565 A1 describes how sulfur corrosion of a copper alloy can be reduced by introducing, in addition to Cu and Zn, a nickel component in the amount of 10-70% by weight as well as an oxidizable alloy ingredient (Zn, Mn, Al and Si) into the alloy. An oxide layer is said to suppress the development of a copper sulfide layer.
  • EP 1 281 838 A2 discloses that corrosion due to a sulfur content in lubricating oil can be counteracted by a selected Cu/Zn ratio.
  • Mn, Al, Si are added to improve the hardness of the alloy, with mainly crystallized manganese-silicide hard phases being formed.
  • JP S 61117240 A proposes a copper alloy with weight amounts of 54-64% Cu, 0.5-3% Si, 0.5-2% Al, 3-7% Mn and the remainder Zn, in which hard phase precipitation is present in the form of manganese silicides.
  • the alloy reduces the formation of copper sulfide layers so that it has a lower corrosion tendency as a bearing material for a turbocharger at high exhaust temperatures.
  • DE 41 01 620 C2 describes a copper alloy with a reduced corrosion tendency with respect to lubricating oils that contain sulfur.
  • the alloy composition consists of 11.5-25% by weight Zn, 5-18% by weight Pb, 1-3.5% by weight Mn, 0.3-1.5% by weight Si.
  • the lead content is uniformly distributed.
  • the silicon and manganese alloy constituents are added so that they are present in a stoichiometric ratio to form manganese silicides in order to prevent free silicon from crystallizing out, which would thus cause embrittlement.
  • hard phase precipitation reinforces the surface hardness and therefore reduces the extent of wear.
  • hard phase precipitation in the area near the surface which presents the greatest resistance to wear and smoothing processes, form spatially limited areas with a high mechanical stress, where high temperatures may occur locally. Processes of formation and decomposition of the reaction layer are accelerated in these areas of the component that are exposed to particularly high thermal loads, so that hard phase precipitation may be problematic from the standpoint of corrosion. It should be pointed out here that in the case of hard phase precipitation in the form of coarse grains under mechanical loads, large sections of the inner and outer boundary layers are under mechanical stress, which in turn increases pitting corrosion.
  • U.S. Pat. No. 6,793,468 B2 proposes a copper alloy containing 54-64% by weight Cu, 0.2-3% by weight Si, 0.2-7% by weight Mn, 0.5-3.5% by weight Al and the remainder Zn, with crystalline manganese silicides being present as elongated aligned structures in the copper alloy matrix.
  • the alignment of the hard phases must be provided in the axial direction with respect to a rotating shaft to be supported and/or the opposing body.
  • DE 10 2011 004 856 A1 proposes that the formation of a load-bearing sulfide film be accelerated, because this prevents the seizing of an opposing surface sliding on it when in contact with hot lubricating oil.
  • a copper alloy which is used for this purpose contains 25-45% by weight Zn, 0.3-2% by weight Si, 1.5-6% by weight Mn and the remainder copper, in which crystalline manganese silicide compounds are present in an oriented arrangement.
  • the density of these precipitates is selected so that there is an average inter-grain spacing of 5-30 ⁇ m, which leads to thermal stress on the joint when it comes in contact with the hot lubricating oil, thereby accelerating the development of the desired sulfide film at the surface of the component.
  • EP 0 709 476 B1 proposes a sintered copper alloy as a friction material in a lubricant environment which includes the present phosphorus and sulfur components, where intermetallic hard phases are formed, selected from FeMo, FeCr, FeTi, FeW, FeB and Al 2 O 3 .
  • intermetallic hard phases selected from FeMo, FeCr, FeTi, FeW, FeB and Al 2 O 3 .
  • the alloy consists of 5-40% by weight Zn, 5-40% by weight Ni, 1-5% by weight Si, 0.1-5% by weight Al, 0.5-3% by weight Pb and preferably Sn in an amount of 3-20% by weight with the remainder being copper.
  • the formation of copper sulfide is suppressed by the large amounts of zinc and nickel. Furthermore, nickel silicides which improve the coefficient of friction are also formed.
  • Additional copper-zinc alloys are described in DE 10 2005 059 391 A1, DE 42 40 157 A1 or CH 223 580. These alloys are used to produce brass components used in an oil environment, such as synchronizer rings, for example. These alloys are formulated so that the silicon they contain will completely enter into the formation of silicides. Since manganese is a preferred substance for forming silicide, the amounts of manganese specified in the exemplary alloys are high and usually greatly exceed 2% by weight. The silicon content is adjusted to conform to the silicide-forming portions and is involved with max. 1% by weight in the exemplary alloy specified in the documents referenced above.
  • additives are added to lubricants with the goal of reducing corrosion on a friction surface and thereby reducing the wear due to abrasion.
  • a corrosion inhibitor anti-wear active ingredient
  • zinc dialkyl dithiophosphate is zinc dialkyl dithiophosphate.
  • a phosphate glass that protects the surface of the reaction layer is formed from this additive in the reaction layer. This ideally involves an exchange of the ligands of the additive with alloy elements as well as an incorporation of substrate cations so that a durable reaction layer is formed.
  • the reaction processes that protect the surface depend on the composition of the internal boundary layer of the substrate material.
  • additional additives have an influence on the process and under some circumstances act as protective additives, which protect the surface competitively with respect to adhesion in the adhesion layer.
  • the alloy structure and the thermal processes taking place in the reaction layer with regard to the dissipation of heat and local temperature peaks are also important for layer buildup and decomposition processes. Therefore, depending on the respective tribological system, the involvement of corrosion inhibitors may even lead to an unwanted chemical decomposition process involving the friction layer under some circumstances.
  • the corrosion-resistant copper alloys known so far are therefore adapted individually to a very specific lubricant system.
  • the formation of the reaction layer can also be influenced not only by such additives that are added to the lubricant with the goal of altering the surface of the friction surface, but also by those added primarily for the purpose of protecting or improving the base oil.
  • Oxidation processes operative or decomposition processes involving additives may then occur, influencing the exchange with the adsorption layer on the friction surface in addition to the uptake of wear particles.
  • replacing the base oil of the lubricant also results in a fundamental change in the tribological system.
  • base oils in the form of mineral oils, hydrocracking oils or synthetic oils such as poly- ⁇ -olefins or esters are being used for lubricants that are modified to be used as gear oils.
  • replacement of the base oil with vegetable oils or animal fats can lead to fundamental changes in the adhesion properties because vegetable oils typically have a high polarity and thus promote an affinity for a metal surface.
  • the changes in the tribological system caused by the change in the lubricant, in particular its base oil so far mostly result in the necessity for adjusting the alloy composition of the friction partners in order to maintain the corrosion-preventing effect.
  • the present disclosure relates a copper alloy having a high corrosion resistance for a wide range of different lubricants, in particular different base oils and a variation of lubricant additives.
  • the property of a low corrosion tendency for different tribological systems is also combined with good mechanical properties, and a high strength in particular.
  • the alloy has a low wear and a coefficient of friction that is adaptive for use as a synchronizer ring in a friction pairing with steel.
  • FIG. 1 shows sliding friction values measured using semi-finished products produced from an alloy according to the present disclosure in three different lubricants A (titanium EG 52512), B (BOT 350 M3) and C (BOT 402);
  • FIG. 2 shows a scanning electron micrograph of a semi-finished product produced from the alloy of FIG. 1 with labeled measurement points for analysis by x-ray photoelectron spectroscopy;
  • FIG. 3 shows the results of wear experiments with the alloy of FIG. 1 in the lubricants A, B, and C of FIG. 1 .
  • the disclosed alloy a special brass alloy—and/or the workpiece manufactured from it (i.e., a synchronizer ring) is/are characterized by a high oil compatibility for a wide range of lubricant systems.
  • the alloy of the present disclosure forms particularly stable reaction layers in different tribological systems under the influence of friction and thermal stress, with leveling and abrasion processes involving the inner boundary layer being substantially retarded. Stabilization of the boundary layer results for the selected ratio between the alloy constituents Si, Cu and Zn. The ratio of the amount of free silicon in comparison with the sum of the alloy constituents copper and zinc is of particular importance.
  • the effect of the zinc component is seen as stabilizing the reaction layer by making available a sufficient reactivity for rapid formation of a layer and healing.
  • An effect somewhat to the contrary is achieved by the silicon component. It is important here for free silicon that is not bound in silicides to be present in dissolved form in the matrix or in silicon-containing non-silicide phases in a weight amount of at least 0.4%. The advantageous effect already occurs when the free silicon content is above the threshold of individual contaminants of 0.15% by weight. The minimum weight amount of 0.4% leads to a definite stabilization of the reaction layer. An even greater amount of free silicon of preferably at least 0.5%, and in particular preferably at least 0.6%, increases the desired effect on the development of the reaction layer, wherein an upper limit is given by the requirement for processability of the alloy.
  • Silicon-rich ⁇ phases which yield mechanically unfavorable alloy properties, should be avoided. It is therefore preferable for the amount of free silicon by weight to be limited to max. 2% and especially preferably to max. 1.5%. With the selected limit for the absolute silicon content, stresses in the cast alloy that can lead to cracking under some circumstances are suppressed, and an advantageous breaking strength of the alloy is maintained.
  • the weight ratio between the alloy constituent zinc and the absolute silicon content is in the range of 10-40 and preferably in the range of 20-35. If the zinc content relative to the amount of free silicon in the alloy matrix is taken into account, the quotient is preferably between 15 and 75 and preferably between 20 and 55. The balance mentioned below between the component zinc, which increases the reactivity, and the free silicon content, which influences the reaction rate, is adjusted so that the formation of the reaction layer takes place selectively with regard to the lubricant additives involved.
  • Silicon in free form acts as an inhibitor of oxidation of other alloy constituents, and in particular reduces the oxidation tendency of zinc so that zinc oxide layers are formed only to a minor extent and instead zinc is present in elemental form for incorporation into the reaction layer. It is additionally assumed that the free silicon in the special brass reduces the diffusion rate of third elements and also reduces the heat transfer within the alloy. This influences the kinetics of the formation of the reaction layer to the extent that the synthesis processes are retarded while at the same time taking place more selectively.
  • intermetallic hard phases there may be a mixture of silicides and aluminides containing only silicon and/or aluminum but also the alloy constituents manganese, iron and nickel as well as the optional element chromium.
  • the selected aluminum content in the alloy results in the formation of primarily aluminum intermetallic phases, thus the elements that are otherwise necessary for the formation of silicide are captured.
  • a silicon content remains as an excess and may be present as free silicon dissolved in the alloy matrix.
  • the weight ratio of the alloy contents is adjusted for a preferred embodiment of the invention, so that the aluminum content exceeds the stoichiometric ratio for the sum of the iron, manganese, nickel and chromium contents.
  • the required minimum amount of 0.4%, preferably at least 0.5% and especially preferably at least 0.6% free silicon is derived for the present multi-component system not only through a sufficiently large amount of aluminum, so that aluminides are formed in competition with silicides, but also from another influencing factor on the solubility of silicon leading to the adjustment of the alloy structure which can be controlled through the absolute zinc content. If there is only or predominantly a ⁇ -brass, then there is a good solubility for silicon in the alloy matrix. Within the predetermined alloy limits, combination amounts are possible in which the ⁇ phase is thermodynamically stable below 600° C. and in which free silicon is soluble only to a lesser extent than in the ⁇ phase.
  • the required minimum amount of 0.4%, preferably at least 0.5% and especially preferably at least 0.6% free silicon is established by the fact that a ⁇ phase content is frozen into the alloy due to the selected cooling conditions after melting of the alloy and possibly additional heat-forming and annealing steps.
  • Cobalt may be present in the alloy in the amount of max. 1.5% by weight. However, an embodiment in which the cobalt content is ⁇ 0.7% by weight or the alloy is more or less free of cobalt is preferred.
  • a lead content of max. 0.8% by weight is basically considered to be an impurity. It was surprising to find that the special oil compatibility of the alloy described here is also achieved even if it is free of Pb. This was surprising against the background that the state-of-the-art alloys must contain a certain amount of Pb in order to achieve oil compatibility. Alloys according to the present disclosure whose Pb content is ⁇ 0.1% by weight are considered to be free of Pb within the scope of these embodiments.
  • the alloy according to the present disclosure it has also been possible to introduce other elements into the formation of silicide, such as nickel and/or iron, for example, despite the fact that they have a significantly lower affinity for formation of silicide in comparison with manganese.
  • the claimed alloy also contains aluminum as an alloy constituent; aluminides may be formed with the elements iron and/or nickel but the affinity for formation of silicide is predominant.
  • Workpieces produced from the alloy according to the present disclosure ensure the buildup of an internal boundary layer in interaction with the lubricant, which permits good adhesion of reaction layers in addition to providing a high thermal and mechanical stability. It is assumed that this unexpected property is the result of an adapted diffusion capability which has an effect on the layer growth of the reaction layer as well as opening up the possibility of using a self-lubricating component as additional corrosion protection.
  • the addition of tin to the alloy composition serves this purpose as it reaches, through diffusion, the friction surface, where it has a self-lubricating effect.
  • a reforming and heat treatment are preferably carried out after bonding the alloy constituents so that a ⁇ phase is formed with a matrix content of at least 70% and preferably more than 80%.
  • the result is a high workpiece hardness and a great resistance to abrasive wear such that a final precipitation hardening is unnecessary for many applications.
  • the amount of the optional ingredient cobalt in the alloy may be reduced. It is preferable to omit cobalt entirely except for unavoidable impurities.
  • the broadband oil compatibility of the required alloy composition is further improved with an amount of cobalt of less than 0.7% by weight. It is therefore assumed that in the present multi-component system, there is an interaction between cobalt fractions and iron fractions and also with chromium, which has an indirect effect on the free silicon content.
  • an increase in the positive properties of the aforementioned alloy can be achieved with a copper alloy containing the following amounts by weight:
  • this alloy is suitable for producing components that are used in an oil environment, such as synchronizer rings, bearing parts or the like.
  • These additional applications also include bushings used as bearing parts. It is self-evident here that the special properties of the workpieces produced from such an alloy are established in particular when they are exposed to manganese lubrication at least temporarily in their oil environment.
  • alloys made of the following composition are preferred for bearing parts because of strength criteria, in particular when the components made of these alloys are to be exposed to higher mechanical loads (amounts given in % by weight):
  • the extruded semi-finished products investigated have a great toughness and sufficient strength plus a high elongation at break.
  • Workpieces and/or semi-finished products with a hardness HB of 2.5/62.5 in the range of 250-270 can be obtained. Since this strength level is sufficient for many applications, the workpieces produced from this alloy do not require any subsequent hardening. In the case of workpieces made of previously known alloys, such a hardness can be achieved only with the additional step of hardening.
  • Tensile tests have shown a 0.2% strain limit in the range of 650-750 MPa.
  • the alloy according to the invention has a sliding friction value of ⁇ 0.1. This is illustrated in FIG. 1 , where the A experiments were conducted in the lubricant titanium EG 52512, the B experiments conducted in the lubricant BOT 350 M3, and the C experiments were conducted in the lubricant BOT 402.
  • FIG. 2 shows a micrograph with labeled measurement points for analysis by x-ray photoelectron spectroscopy (EDX).
  • EDX x-ray photoelectron spectroscopy
  • FIG. 3 shows the results of wear experiments with the experimental alloy in the lubricants mentioned above, namely A (titanium EG 52512), B (BOT 350 M3) and C (BOT 402) which had the broadband oil compatibility.
  • A titanium EG 52512
  • B BOT 350 M3
  • C BOT 402
  • the buildup of a stable reaction layer was detected, with the experiments being carried out at an oil temperature of 80° C., a surface pressure of 50 MPa and a sliding speed of 1 m/s. After traveling a friction distance of 100 km, the wear resistance values were within a relatively narrow range of 140-170 km/g. It was surprising to find that in the wear experiments already described, the sample piece not only exhibited a particularly broadband oil compatibility but also the respective wear resistance was high and the range covered by the wear resistance values thus determined is quite narrow, despite the use of different varieties of oil.
  • an alloy composition having the following elements indicated in % by weight would be suitable for this purpose:
  • Oil compatibility tests were performed for this alloy group using two different types of alloys that differ from one another with regard to their nickel and aluminum content. It is interesting that the oil compatibility results achieved with these alloys show that, despite the absence of lead as an alloy ingredient, the oil compatibility corresponds to that found for the alloy containing Pb described above. These are the types of Pb-free alloys that were tested (amount in % by weight), wherein free silicon is preferably present in the alloy matrix or in non-silicide phases containing silicon in the amount of least 0.4%, preferably at least 0.5% and especially preferably at least 0.6%:
  • a sample of alloy type 1 was tested specifically with regard to its oil compatibility and found to have the following composition (amount in % by weight):
  • composition of the sample tested from alloy type 2 had the following composition (amounts in % by weight):
  • Bushings as bearing parts could be produced from such an alloy with the process steps that are known per se. This includes the following steps:

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  • Chemical & Material Sciences (AREA)
  • General Engineering & Computer Science (AREA)
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  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
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  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)
  • Mechanical Operated Clutches (AREA)
  • Lubricants (AREA)
  • Gears, Cams (AREA)
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DE102014101343.3 2014-02-04
DE102014101343 2014-02-04
PCT/EP2015/052229 WO2015117972A2 (de) 2014-02-04 2015-02-04 Schmierstoffverträgliche kupferlegierung

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US11572606B2 (en) 2018-10-29 2023-02-07 Otto Fuchs Kommanditgesellschaft High-tensile brass alloy and high-tensile brass alloy product

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US11427890B2 (en) 2014-02-04 2022-08-30 Otto Fuchs Kommanditgesellschaft Lubricant-compatible copper alloy
US10316398B2 (en) * 2014-05-16 2019-06-11 Otto Fuchs Kommanditgesellschaft High-tensile brass alloy and alloy product
US20190017149A1 (en) * 2016-05-20 2019-01-17 Otto Fuchs Kommanditgesellschaft High Tensile Brass Alloy and High Tensile Brass Alloy Product
US10570484B2 (en) * 2016-05-20 2020-02-25 Otto Fuchs Kommanditgesellschaft High tensile brass alloy and high tensile brass alloy product
US11359263B2 (en) 2016-05-20 2022-06-14 Otto Fuchs Kommanditgesellschaft Lead-free high tensile brass alloy and high tensile brass alloy product
US11572606B2 (en) 2018-10-29 2023-02-07 Otto Fuchs Kommanditgesellschaft High-tensile brass alloy and high-tensile brass alloy product
US20220136085A1 (en) * 2020-10-29 2022-05-05 Otto Fuchs - Kommanditgesellschaft Lead-free Cu-Zn alloy

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US11427890B2 (en) 2022-08-30
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JP6255501B2 (ja) 2017-12-27
KR20160115928A (ko) 2016-10-06
KR101820036B1 (ko) 2018-01-18
CN105980586B (zh) 2017-10-31
EP3102713B1 (de) 2018-07-18
CN105980586A (zh) 2016-09-28
KR20170070263A (ko) 2017-06-21
ES2688034T3 (es) 2018-10-30
RU2661960C1 (ru) 2018-07-23
WO2015117972A2 (de) 2015-08-13
US20200024694A1 (en) 2020-01-23
EP3102713A2 (de) 2016-12-14
BR112016014727B1 (pt) 2021-06-29

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