EP3423604B1 - Alliage de cuivre contenant de l'étain, procédé pour sa préparation ainsi que son utilisation - Google Patents

Alliage de cuivre contenant de l'étain, procédé pour sa préparation ainsi que son utilisation Download PDF

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EP3423604B1
EP3423604B1 EP17706407.8A EP17706407A EP3423604B1 EP 3423604 B1 EP3423604 B1 EP 3423604B1 EP 17706407 A EP17706407 A EP 17706407A EP 3423604 B1 EP3423604 B1 EP 3423604B1
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tin
phases
alloy
copper alloy
phase
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EP3423604A1 (fr
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Kai Weber
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Wieland Werke AG
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Wieland Werke AG
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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
    • C22C9/02—Alloys based on copper with tin 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02—Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/025—Casting heavy metals with high melting point, i.e. 1000 - 1600 degrees C, e.g. Co 1490 degrees C, Ni 1450 degrees C, Mn 1240 degrees C, Cu 1083 degrees C

Definitions

  • the invention relates to a tin-containing copper alloy with excellent hot and cold formability, high resistance to abrasive wear, adhesive wear and fretting wear and improved corrosion resistance and stress relaxation resistance according to the preamble of one of claims 1 to 3, a method for their production according to the preamble of the claims 10 to 11 and their use according to the preamble of claims 17 to 19.
  • copper-tin alloys Due to the alloy component tin, copper-tin alloys are characterized by high strength and hardness. The copper-tin alloys are also considered to be corrosion-resistant and seawater-resistant.
  • This group of materials has a high level of resistance to abrasive wear.
  • the copper-tin alloys ensure good sliding properties and high fatigue strength, which results in their excellent suitability for sliding elements and sliding surfaces in engine and vehicle construction as well as in general mechanical engineering.
  • an addition of lead is added to the copper-tin alloys for plain bearing applications to improve the emergency running properties and the machinability.
  • Copper-tin alloys are widely used in the electronics and telecommunications industries. They often have sufficient electrical conductivity and good to very good spring properties. The Adjustment of the spring properties requires sufficient cold formability of the materials.
  • percussion instruments are preferably made from copper-tin alloys because of their special sound properties.
  • Two types of copper-tin alloys with 8 and 20% by weight of tin are particularly widespread.
  • the copper-tin materials have a particularly strong tendency to absorb gas with subsequent pore formation and segregation phenomena due to their wide solidification interval.
  • the Sn-rich segregations can only be removed to a very limited extent with a homogenization annealing following the casting process.
  • the susceptibility of copper-tin alloys to pores and segregation increases as the Sn content increases.
  • the element phosphorus is added to the copper-tin alloys in order to sufficiently deoxidize the melt.
  • phosphorus also extends the solidification interval of copper-tin alloys, which results in an increased susceptibility to pores and segregation of this group of materials.
  • the description of a process for the production of shaped pieces from copper-tin alloys which contain 6 to 14% by weight of Sn, over 0.1% by weight of P, preferably 0.2 to 0.4% by weight of P , which can be replaced by silicon, boron or beryllium.
  • the copper-tin alloy has about 91.2% by weight Cu, about 8.5% by weight Sn and about 0.3% P. Accordingly, prior to final processing by cold forming or hot forming, the castings are homogenized at a temperature below 700 ° C. until the eutectoids enriched in tin and phosphorus dissolve.
  • Vibration wear also known as fretting in technical terms, is frictional wear that occurs between oscillating contact surfaces.
  • fretting In addition to the geometrical and / or volume wear of the components, the reaction with the surrounding medium leads to fretting corrosion.
  • the material damage can significantly reduce the local strength in the wear zone, in particular the fatigue strength. Vibration cracks can originate from the damaged component surface, leading to fatigue failure / frictional fatigue failure. With fretting corrosion, the fatigue strength of a component can drop well below the fatigue strength of the material.
  • the mechanism of vibratory frictional wear differs considerably from the types of sliding wear with unidirectional movement. In particular, the effects of corrosion are particularly pronounced during frictional wear.
  • connection elements In motors and machines, electrical connectors are often arranged in an environment in which they are exposed to mechanical vibratory movements. If the elements of a connection arrangement are located on different assemblies which move relative to one another as a result of mechanical loads, a corresponding relative movement of the connection elements can occur. These relative movements lead to frictional wear and to fretting corrosion of the contact zone of the connector. Microcracks form in this contact zone, which greatly reduces the fatigue strength of the connector material. This can result in failure of the connector due to fatigue failure. Furthermore, there is an increase in contact resistance due to fretting corrosion.
  • 32 536 C1 contains a regulation on how the fretting corrosion behavior of connectors can be improved on the material side.
  • a contact material made of a silver, palladium or palladium-silver alloy with a content of 20 to 50% by weight tin, indium and / or antimony is applied to a carrier made of bronze, for example.
  • the silver and / or palladium content ensures corrosion resistance.
  • the oxides of tin, indium and / or antimony increase the wear resistance.
  • the Consequences of fretting corrosion are countered.
  • Alloying with metalloids such as boron, silicon and phosphorus achieves the lowering of the relatively high base melting temperature, which is important from a processing point of view.
  • the alloying elements boron and silicon in particular are responsible for the sharp reduction in the melting temperature of hard nickel-base alloys, which is why their use as self-fluxing hard nickel-base alloys is possible.
  • a particularly high P content of 0.2 to 0.6% by weight is specified with an Si content of the alloy of 0.05 to 0.15% by weight. This underlines the ostensible demand for the self-flowing properties of the material. With this high P content, however, the options for hot formability of the alloy will be severely limited.
  • the silicon borides which are mostly in the form of the modifications SiB 3 , SiB 4 , SiB 6 and / or SiB n, which are determined by the boron content, differ significantly from silicon in their properties. These silicon borides have a metallic character, which is why they are electrically conductive. They have an extremely high temperature and oxidation resistance.
  • the modification of SiB 6 which is preferred for sintered products, is used, for example, in ceramic production and processing because of its very high hardness and high abrasive wear resistance.
  • the invention is based on the object of providing a copper-tin alloy which has excellent hot formability over the entire range of the tin content.
  • a starting material can be used that was produced by conventional casting processes without the absolute necessity of carrying out spray compacting or thin strip casting.
  • the copper-tin alloy should be free of gas and shrinkage pores as well as stress cracks and be characterized by a structure with a uniform distribution of the Sn-rich ⁇ -phase that is present depending on the Sn content of the alloy.
  • the as-cast state of the copper-tin alloy does not necessarily have to be homogenized by means of a suitable annealing treatment in order to be able to produce sufficient hot formability.
  • Even the casting material should be characterized by high strength, high hardness and high corrosion resistance.
  • a fine-grain structure with high strength, high hardness, high stress relaxation and corrosion resistance, high electrical conductivity and a high degree of complex wear resistance can be set by means of further processing that includes annealing or hot forming and / or cold forming with at least one annealing.
  • the invention is represented by the features according to one of Claims 1 to 3, with regard to a production method by the features of Claims 10 to 11 and with regard to a use by the features of Claims 17 to 19.
  • the further back-referenced claims relate to advantageous designs and developments of the invention.
  • Sn-rich segregations are understood to mean accumulations of the ⁇ -phase in the cast structure, which are designed as so-called reverse block segregation and / or grain boundary segregation, which cause damage to the structure in the form of cracks when the casting is subjected to thermal and / or mechanical stress Break. After casting, the structure is still free of gas pores and shrinkage pores as well as stress cracks.
  • the alloy is in the as-cast state.
  • the Sn-rich ⁇ phase is preferably at least 1% by volume.
  • the Sn-rich ⁇ -phase is distributed evenly in the structure in an island-like and / or network-like and / or line-like stretched manner.
  • the alloy is in a further processed state.
  • the invention is based on the consideration that a tin-containing copper alloy in the cast state as well as in the further processed state with Al-containing and B-containing phases, Si-containing and B-containing phases and / or addition compounds and / or mixed compounds two phases is provided, which can be produced by means of the sand casting, shell mold casting, investment casting, full mold casting, die casting and permanent mold casting process or with the aid of the continuous or semi-continuous continuous casting process.
  • process engineering complex and cost-intensive primary forming techniques is possible, but is not an absolute necessity for the production of the tin-containing copper alloy according to the invention.
  • spray compacting can be dispensed with.
  • the casting formats of the tin-containing copper alloy according to the invention can be hot-formed directly over the entire range of the Sn content without performing homogenization annealing, for example by hot rolling, extrusion or forging. This largely removes the processing restrictions that previously existed in the manufacture of semi-finished products and components made of copper-tin alloys and which led to this group of materials being subdivided into Cu-Sn wrought alloys and Cu-Sn cast alloys.
  • the matrix of the structure of the tin-containing copper alloy in the as-cast state consists of increasing proportions of ⁇ -phase (Sn-rich) in otherwise ⁇ -phase (Sn-poor) with increasing Sn content of the alloy, depending on the casting process.
  • the form of the arrangement of the ⁇ phase in the structure also changes. It has been found that in the Sn content range from 4.0 to 9.0% by weight, the ⁇ phase is distributed uniformly in the structure with up to 40% by volume, predominantly in island form. If the Sn content of the alloy is between 9.0 and 13.0% by weight, the island shape of the ⁇ phase, which is present in the structure with up to 60% by volume, changes into the network shape. This ⁇ network is also distributed very evenly in the structure of the alloy. In the Sn content range from 13.0 to 17.0% by weight, the ⁇ phase with up to 80% by volume is almost exclusively in the form of a uniform network in the structure. With an Sn content of the alloy of 17.0 to 23.0% by weight, the structural fraction of the ⁇ -phase arranged as a dense network in the structure is up to 98% by volume.
  • the elements boron, silicon and phosphorus in particular take on a deoxidizing function in the melt of the invention. This counteracts the formation of tin oxides in the tin-containing copper alloy.
  • By adding boron and silicon it is possible to lower the phosphorus content without lowering the intensity of the deoxidation of the melt. This measure succeeds in suppressing the adverse effects of adequate deoxidation of the melt by means of an addition of phosphorus.
  • a high P content would also extend the already very large solidification interval of the tin-containing copper alloy, which would result in an increase in the susceptibility to pores and segregation of this type of material. In addition, an increased formation of the copper-phosphorus phase would be the result.
  • This type of phase is considered to be one of the reasons for the hot brittleness of tin-containing copper alloys.
  • the disadvantageous effects of the addition of phosphorus are reduced by limiting the P content in the alloy according to the invention to the range from 0.001 to 0.08% by weight.
  • the elements boron, silicon and aluminum are of particular importance in the tin-containing copper alloy according to the invention.
  • the phases of the Al-B, Si-B systems and / or their addition compounds and / or mixed compounds already separate in the melt.
  • the Si-B phases known as silicon borides can be present in the modifications SiB 3 , SiB 4 , SiB 6 and SiB n .
  • the symbol "n" in the latter modification is based on the fact that boron has a high solubility in the silicon lattice.
  • the Al-B phases named as aluminum borides can mostly be present in the structure in the modifications AlB 2 and / or AlB 12.
  • they take on the function of crystallization nuclei during solidification and cooling. As a result, there is no longer the need to add so-called foreign nuclei to the melt, the even distribution of which in the melt can only be inadequately guaranteed.
  • the as-cast state of the invention has a very uniform structure with a fine distribution of the ⁇ -phase in the form of evenly and densely arranged islands and / or in the form of a uniformly dense network. Accumulations of the Sn-rich ⁇ -phase, which are formed as so-called reverse block segregation and / or as grain boundary segregation, cannot be observed in the cast structure of the invention.
  • the elements boron, silicon, aluminum and phosphorus cause a reduction in the metal oxides.
  • the elements themselves are oxidized, rise to the surface of the castings and form there, as borosilicates and / or borophosphosilicates and / or aluminum oxide-borosilicates and / or aluminum oxide-borophosphosilicates, together with the phosphorus silicates and aluminum oxides, a protective layer that protects the castings from gas absorption .
  • Exceptionally smooth surfaces of the castings made of the alloy according to the invention were found, which indicate the formation of such a protective layer.
  • the structure of the as-cast state of the invention was also free of gas pores over the entire cross-section of the cast parts.
  • a basic idea of the invention consists in the transfer of the effect of borosilicates and phosphorus silicates with regard to the adjustment of the different thermal expansion coefficients of the joining partners during diffusion soldering to the processes during casting, hot forming and thermal treatment of the copper-tin materials. Because of the wide solidification interval of these alloys, large mechanical stresses occur between the staggered crystallizing Sn-poor and Sn-rich structural areas, which lead to cracks and so-called shrinkage pores. Furthermore, these damage features can also occur during hot forming and high-temperature annealing of the copper-tin alloys due to the different hot forming behavior and the different thermal expansion coefficients of the Sn-poor and Sn-rich structural components.
  • the combined addition of boron, silicon, aluminum and phosphorus to the tin-containing copper alloy according to the invention causes, on the one hand, a uniform structure with a fine distribution of the structural components with different Sn content during the solidification of the melt by means of the action of the hard particles as crystallization nuclei.
  • the borosilicates and / or borophosphosilicates and / or aluminum oxide-borosilicates and / or aluminum oxide-borophosphosilicates that form during the solidification of the melt, together with the phosphorus silicates, ensure the necessary adjustment of the thermal expansion coefficients of the Sn-poor and Sn-rich phases . This prevents the formation of pores and stress cracks between the phases with different Sn contents.
  • the alloy according to the invention can be subjected to further processing by annealing or by hot forming and / or cold forming in addition to at least one annealing.
  • the hard particles as crystallization nuclei which, together with the borosilicates and / or borophosphosilicates and / or aluminum oxide-borosilicates and / or aluminum oxide-borophosphosilicates and with the phosphorus silicates, bring about an equalization of the thermal expansion coefficients of the Sn-poor and Sn-rich phases, could also bring about an equalization of the thermal expansion coefficients of the Sn-poor and Sn-rich phases during the hot forming process of the tin-containing copper alloy according to the invention to be watched.
  • the hard particles serve as recrystallization nuclei.
  • the hard particles are to be made responsible for the fact that the dynamic recrystallization takes place favorably during the hot forming of the alloy according to the invention. This results in a further increase in the uniformity and fine-grainedness of the structure.
  • an exceptionally smooth surface of the parts could also be determined after hot forming of the castings.
  • This observation indicates the formation of borosilicates and / or borophosphosilicates and / or aluminum oxide-borosilicates and / or aluminum oxide-borophosphosilicates as well as of phosphorus silicates and aluminum oxides, which takes place in the material during hot forming.
  • the silicates and hard particles require an equalization of the different thermal expansion coefficients of the Sn-poor and Sn-rich components even during hot forming.
  • the structure was free of cracks and pores even after hot forming.
  • the role of the hard particles as nuclei for the static recrystallization became apparent during the annealing treatment after cold forming.
  • the outstanding function of the hard particles as nuclei for the static recrystallization manifested itself in the lowering of the necessary recrystallization temperature which has become possible, which additionally facilitates the establishment of a fine-grain structure of the alloy according to the invention.
  • the level of the parameter R p0.2 is important for the sliding elements and guide elements in internal combustion engines, valves, turbochargers, transmissions, exhaust gas aftertreatment systems, lever systems, brake systems and joint systems, hydraulic units or in machines and systems in general mechanical engineering. Furthermore, a high value of R p0.2 is a prerequisite for the necessary spring properties of connectors in electronics and electrical engineering.
  • the Sn content of the invention ranges between 4.0 and 23% by weight.
  • a tin content of less than 4.0% by weight would result in too low strength values and hardness values.
  • the running properties would be inadequate in the event of a sliding load.
  • the resistance of the alloy to abrasive and adhesive wear would not meet the requirements. If the Sn content exceeds 23.0% by weight, the toughness properties of the alloy according to the invention would deteriorate rapidly, as a result of which the dynamic load-bearing capacity of the components made of the material is reduced.
  • the alloy according to the invention Due to the precipitation of the hard particles, the alloy according to the invention has a hard phase component which, due to its high hardness, contributes to an improvement in the material resistance to abrasive wear.
  • the proportion of hard particles results in improved resistance to adhesive wear, since these phases show a low tendency to weld with a metallic counter-rotating partner in the event of sliding stress. They thus serve as an important wear carrier in the tin-containing copper alloy according to the invention.
  • the hard particles increase the heat resistance and the stress relaxation resistance of components from the invention. This represents an important prerequisite for the use of the alloy according to the invention, in particular for sliding elements and for components, line elements, guide elements and connecting elements in electronics / electrical engineering.
  • borosilicates and / or borophosphosilicates and / or aluminum oxide-borosilicates and / or aluminum oxide-borophosphosilicates and of phosphorus silicates in the alloy according to the invention not only leads to a significant reduction in the pores and cracks in the structure. Together with the aluminum oxides, these silicate phases also take on the role of a wear-protecting and / or corrosion-protecting coating on the components.
  • the alloy according to the invention thus ensures a combination of the properties of wear resistance and corrosion resistance.
  • This combination of properties leads to a high resistance to the mechanisms of sliding wear, as required, and to a high material resistance to fretting corrosion.
  • the invention is outstandingly suitable for use as a sliding element and plug connector, since it has a high degree of resistance to sliding wear and vibrational friction wear / fretting.
  • the effect of the hard particles as crystallization nuclei and recrystallization nuclei, as wear carriers and the effect of the Al oxides and the silicate phases for the purpose of corrosion protection can only reach a technically significant level in the alloy according to the invention if the silicon content is at least 0.05 wt. %, the aluminum content is at least 0.01% by weight and the boron content is at least 0.005% by weight.
  • the Si content exceeds 2.0% by weight and / or the Al content exceeds 1.0% by weight and / or the B content exceeds 0.6% by weight, this leads to a Deterioration of the casting behavior.
  • the excessively high content of hard particles would make the melt significantly more viscous.
  • reduced toughness properties of the alloy according to the invention would be the result.
  • the range for the Si content within the limits of 0.05 to 1.5 is advantageous % By weight and especially from 0.5 to 1.5% by weight.
  • the advantageous Al content of the alloy according to the invention is 0.1 to 0.8% by weight.
  • boron a content of 0.01 to 0.6% by weight is considered to be advantageous.
  • the boron content of 0.1 to 0.6% by weight has proven to be particularly advantageous.
  • the setting of a specific element ratio of the elements silicon and boron has proven to be important.
  • the Si / B ratio of the element contents (in% by weight) of the elements silicon and boron in the alloy according to the invention is between 0.3 and 10.
  • a Si / B ratio of 1 to 10 and furthermore of 1 to 6 has proven to be good proven beneficial.
  • the precipitation of the hard particles influences the viscosity of the melt of the alloy according to the invention. This fact also underlines why the addition of phosphorus must not be dispensed with. Phosphorus has the effect that the melt is sufficiently thin despite the content of hard particles, which is of great importance for the castability of the invention.
  • the phosphorus content of the alloy according to the invention is 0.001 to 0.08% by weight. A P content in the range from 0.001 to 0.05% by weight is advantageous.
  • the sum of the element contents of the elements silicon, boron and phosphorus is advantageously at least 0.5% by weight.
  • Machine processing of semi-finished products and components from the conventional copper-tin and copper-tin-phosphorus wrought alloys, in particular with an Sn content of up to approx. 9% by weight, is only possible with great effort due to the inadequate machinability.
  • the occurrence of long helical chips in particular causes a long time
  • the hard particles in the regions of which, depending on the Sn content of the alloy, the element tin and / or the ⁇ phase is crystallized or precipitated, serve as chip breakers.
  • the resulting short crumbling chips and / or tangled chips facilitate the machinability, which is why the semi-finished products and components made from the alloy according to the invention have better machinability.
  • the Sn-rich ⁇ phase is arranged uniformly in island form with up to 40% by volume.
  • the element tin and / or the ⁇ -phase is mostly crystallized and / or coated in the areas of the hard particles.
  • the castings of these embodiments have excellent hot formability at the working temperature in the range from 600 to 880 ° C.
  • the significant increase in strength and hardness after the hot forming process step can be used for components that do not require cold forming for their manufacture.
  • accelerated cooling advantageously in water, can preferably take place after the hot forming.
  • the hard particles precipitated in the structure act as recrystallization nuclei during the thermal treatment at a temperature of 200 to 880 ° C with a duration of 10 minutes to 6 hours of the cold-formed material state.
  • This further processing step it is possible to set a structure with a grain size of up to 20 ⁇ m.
  • the promotion of the recrystallization mechanisms by the hard particles allows the recrystallization temperature to be lowered so that a structure with a grain size of up to 10 ⁇ m can be created.
  • a multi-stage production process consisting of cold forming and annealing and / or by appropriately lowering the recrystallization temperature, it is even possible to set the size of the crystallites in the material structure to below 5 ⁇ m.
  • the mechanical properties of some embodiments are representative of the entire range of alloy compositions and production parameters.
  • the results of the investigation of corresponding exemplary embodiments described below make it clear that values for the tensile strength R m of over 700 to 800 MPa, values for the yield strength R p0.2 of over 600 to 700 MPa can be achieved.
  • the toughness properties of the embodiments are at a very high level. This fact is expressed by the high values for the elongation at break A5.
  • the structure of these embodiments of the invention is characterized by a content of ⁇ -phase of up to 60% by volume, this type of phase being evenly distributed in the structure in island form and network form.
  • the element tin and / or the ⁇ -phase is mostly crystallized and / or coated in the areas of the hard particles.
  • the castings of these embodiments have excellent hot formability at the working temperature in the range from 600 to 880 ° C.
  • the structure of the embodiments is very fine-grained after the hot forming. Due to the high strength values of the hot-formed state, its cold formability is limited. This can be significantly improved by an annealing treatment after the hot forming process at a temperature of 200 to 880 ° C with a duration of 10 minutes to 6 hours.
  • the hard particles precipitated in the structure act as recrystallization nuclei during the thermal treatment at a temperature of 200 to 880 ° C with a duration of 10 minutes to 6 hours of the cold-formed material state.
  • This further processing step it is possible to set a finer-grain structure.
  • the promotion of the recrystallization mechanisms by the hard particles allows the recrystallization temperature to be lowered so that a structure with a further reduced grain size can be produced.
  • the fine-grain structure of the structure can be further optimized through a multi-stage production process consisting of cold forming and annealing.
  • the ⁇ -phase in the cast structure of these embodiments of the invention is in the form of a uniformly arranged network with up to 80% by volume.
  • the structure can have dendritic structural components, which, however, also have a network-like character due to the very small distance between the so-called dendrite arms.
  • the element tin and / or the ⁇ -phase is mostly crystallized and / or encased in the areas of the hard particles.
  • the castings of these embodiments also have excellent hot formability at the working temperature in the range from 600 to 880 ° C. It is precisely in this content range for the alloying element tin of 13.0 to 17.0% by weight that the conventional copper-tin alloys can only be thermoformed with great difficulty without the occurrence of hot cracks and hot fractures.
  • the structure of the embodiments is very fine-grained after the hot forming. Due to the high strength values of the hot-formed state, its cold formability is severely limited.
  • An annealing treatment after the hot forming process at a temperature of 200 to 880 ° C with a duration of 10 minutes to 6 hours can improve the cold formability of the semi-finished products.
  • the structural feature of crystallization of the element tin and / or the ⁇ -phase in the areas of the hard particles and / or the coating of these hard particles with the element tin and / or the ⁇ -phase is more fully pronounced with regard to the as-cast state.
  • the hard particles precipitated in the structure act as recrystallization nuclei during the thermal treatment at a temperature of 200 to 880 ° C with a duration of 10 minutes to 6 hours of the cold-formed material state.
  • This further processing step it is possible to set a structure with a grain size of up to 35 ⁇ m.
  • the promotion of the recrystallization mechanisms by the hard particles allows the recrystallization temperature to be lowered so that a structure with a grain size of up to 25 ⁇ m can be created.
  • the network-like arrangement of the ⁇ -phase in the structure is retained.
  • a very dense network of the ⁇ -phase which is evenly arranged with up to 98% by volume in the cast structure, is a feature of these embodiments of the invention.
  • the structure can have more dendritic structural components, which, however, also have a network-like character due to the very small distance between the so-called dendrite arms.
  • the element tin and / or the ⁇ -phase is mostly crystallized and / or encased in the areas of the hard particles.
  • the castings of these embodiments also have excellent hot formability at the working temperature in the range from 600 to 880 ° C.
  • the alloy element tin contributes in particular to the formation of a so-called tribo-layer between the sliding partners. This mechanism is particularly important under mixed friction conditions, when the emergency running properties of a material come to the fore.
  • the tribo layer leads to a reduction in the size of the purely metallic contact area between the sliding partners, which prevents the elements from welding or seizing.
  • the hard particles precipitate in the structure. These phases protect the material from the Consequences of abrasive wear and tear, i.e. before material is removed due to furrow wear. Furthermore, the hard particles have a low tendency to weld with the metallic sliding partner, which is why, together with the complex tribo-layer, they ensure a high adhesive wear resistance of the invention.
  • the hard particles bring about a higher temperature stability of the structure of the copper alloy according to the invention. This results in a high heat resistance and an improvement in the resistance of the material to stress relaxation.
  • the cast variant and the further processed variant of the alloy according to the invention can contain the following optional elements:
  • the element zinc can be added to the tin-containing copper alloy according to the invention in a content of 0.1 to 2.0% by weight. It was found that the alloying element zinc, depending on the Sn content of the alloy, increases the proportion of Sn-rich phases in the invention, thereby increasing strength and hardness. However, no indications could be found that the addition of zinc has a positive effect on the uniformity of the structure and on the further reduction of the content of pores and cracks in the structure. Obviously, the influence of the combined alloy content of boron, silicon and phosphorus predominates. A strength- and hardness-increasing effect could not be observed below 0.1% by weight of Zn.
  • the toughness properties of the alloy were lowered to a lower level.
  • the tin-containing copper alloy of the present invention deteriorated in corrosion resistance.
  • a zinc content in the range from 0.5 to 1.5% by weight can advantageously be added to the invention.
  • the alloying elements iron and magnesium can be added individually or in combination.
  • the alloy according to the invention can contain 0.01 to 0.6% by weight of Fe.
  • Fe iron borides, Fe phosphides and Fe silicides and / or Fe-rich particles are present in the structure.
  • adducts and / or mixed compounds of the containing phases and the Al-containing and B-containing phases, Si-containing and B-containing phases and / or Si-Al-B phases are formed in the structure.
  • These phases and compounds contribute to increasing the strength, hardness, heat resistance, stress relaxation resistance, electrical conductivity and improving the resistance to abrasive and adhesive wear of the alloy. This improvement in properties is not achieved with an Fe content of less than 0.01% by weight. If the Fe content exceeds 0.6% by weight, there is a risk of the iron forming clusters in the structure. This would be associated with a significant deterioration in the processing properties and performance properties.
  • the element magnesium can be added to the alloy according to the invention in an amount of from 0.01 to 0.5% by weight.
  • up to 15% by volume of Mg borides, Mg phosphides and Cu-Mg phases and Cu-Sn-Mg phases are present in the structure.
  • addition compounds and / or mixed compounds of the Mg-containing phases and the Al-containing and B-containing phases, Si-containing and B-containing phases and / or Si-Al-B phases are formed in the structure. These phases and compounds also contribute to increasing the strength, the hardness, the heat resistance, the stress relaxation resistance, the electrical conductivity and the improvement of the resistance to abrasive and adhesive Wear of the alloy.
  • the Mg content is below 0.01% by weight, this improvement in properties is not achieved. If the Mg content exceeds 0.5% by weight, the castability of the alloy in particular deteriorates. In addition, the excessively high content of Mg-containing compounds would significantly impair the toughness properties of the alloy according to the invention.
  • the tin-containing copper alloy can contain a small amount of lead.
  • Lead contents of up to a maximum of 0.25% by weight are still just acceptable and above the contamination limit.
  • the tin-containing copper alloy is free of lead except for any unavoidable impurities.
  • lead contents of up to a maximum of 0.1% by weight of Pb are envisaged.
  • the extensive freedom of the structure from gas pores and shrinkage pores, voids, segregations and cracks in the as-cast state is regarded as a particular advantage of the invention.
  • the alloy composition according to the invention in particular the formation of open porosity can be suppressed during the melting process, as a result of which the compressive strength of the sliding layer is increased.
  • Another particular advantage of the invention is the elimination of the imperative to carry out a special primary molding technique such as spray compacting or thin strip casting to provide a uniform, largely pore-free and segregation-free structure.
  • a special primary molding technique such as spray compacting or thin strip casting
  • conventional casting processes can be used for the primary forming process of the alloy according to the invention.
  • one aspect of the invention excludes a method for the production of end products or of components with a shape close to the end product the tin-containing copper alloy according to the invention with the aid of the sand casting process, shell mold casting process, investment casting process, full mold casting process, die casting process or the lost foam process.
  • one aspect of the invention includes a method for the production of strips, sheets, plates, bolts, round wires, profile wires, round bars, profile bars, hollow bars, tubes and profiles from a tin-containing copper alloy according to the invention with the aid of the permanent mold casting process or the continuous or semi-continuous continuous casting process.
  • the invention no longer has the imperative to use homogenization annealing or solution annealing to distribute or dissolve the Sn-rich ⁇ phase in the structure more finely, or to remove it, depending on the Sn content.
  • the ⁇ -phase which is evenly and finely distributed in the cast structure of the alloy according to the invention with a corresponding Sn content, assumes an essential function for the functional properties of the alloy.
  • the further processing of the as-cast state can include performing at least one hot forming in the temperature range from 600 to 880.degree.
  • the semi-finished products and components can be cooled after hot forming in calmed or accelerated air or with water respectively.
  • the structure of the embodiments is very uniform and fine-grained after the hot forming.
  • the hot worked condition of the invention has extremely high values for strength and hardness.
  • the hard particles of smaller size continued to precipitate during hot forming.
  • the inertia of the precipitation of the Al-containing hard particles they are formed to a greater extent during hot forming.
  • At least one annealing treatment of the as-cast state and / or the hot-formed state of the invention in the temperature range from 200 to 880 ° C with a duration of 10 minutes to 6 hours, alternatively with cooling in calm or accelerated air or with water, can be carried out.
  • One aspect of the invention relates to an advantageous method for further processing the as-cast state or the hot-formed state or the annealed cast state or the annealed hot-formed state, which comprises performing at least one cold forming.
  • At least one annealing treatment of the cold-formed state of the invention can be carried out in the temperature range from 200 to 880 ° C. for a period of 10 minutes to 6 hours.
  • Stress-relieving annealing / aging annealing can advantageously be carried out in the temperature range from 200 to 650 ° C. with a duration of 0.5 to 6 hours.
  • the matrix of the uniform structure of the invention consists of ductile ⁇ -phase with proportions of ⁇ -phase depending on the Sn content of the alloy. Due to its high strength and hardness, the ⁇ phase leads to the alloy's high resistance to abrasive wear. In addition, due to its high Sn content, which results in its tendency to form a tribo-layer, the ⁇ phase increases the resistance of the material to adhesive wear.
  • the hard particles are embedded in the metallic base. In further embodiments of the invention, Fe- and / or Mg-containing phases precipitated in the metallic base material are added.
  • This heterogeneous structure consisting of a metallic base mass of ⁇ - and ⁇ -phase, in which precipitates of great hardness are embedded, gives the subject matter of the invention an outstanding combination of properties.
  • the alloy according to the invention Due to the uniform and fine-grain structure with an extensive absence of pores, freedom from cracks and segregation and the content of hard particles, the alloy according to the invention has a high degree of strength, hardness, ductility, complex wear resistance and corrosion resistance even in the as-cast state. For this reason, the alloy according to the invention has a wide range of uses even in the as-cast state.
  • composite bearing shells or composite bearing bushings can be produced by roll cladding, inductive or conductive roll cladding or by laser roll cladding.
  • Sliding elements and guide elements in internal combustion engines, valves, turbochargers, transmissions, exhaust gas aftertreatment systems, lever systems, brake systems and joint systems, hydraulic units or in machines and systems in general can already be made from the casting formats in strip form, sheet metal form, plate form, bolt form, wire form, rod form, tube form or profile form Mechanical engineering are manufactured.
  • semi-finished products and components with complex geometry and increased mechanical properties and optimized wear properties can be produced for these purposes. This takes into account the increased component requirements in the event of dynamic loading.
  • Another aspect of the invention includes a use of the tin-containing copper alloy according to the invention for components, line elements, guide elements and connecting elements in electronics / electrical engineering.
  • the invention is suitable for the metal objects in structures for the rearing of organisms living in seawater (aquaculture).
  • Another aspect of the invention includes a use of the tin-containing copper alloy according to the invention for propellers, blades, propellers and hubs for shipbuilding, for housings of water pumps, oil pumps and fuel pumps, for idlers, impellers and paddle wheels for pumps and water turbines, for gears, worm wheels, helical gears as well as for pressure nuts and spindle nuts as well as for pipes, seals and connecting bolts in the maritime and chemical industry.
  • Basins in particular, so-called cymbals, of high quality are made from tin-containing copper alloys by means of hot forming and at least one annealing before they are usually brought into their final shape by means of a bell or a bowl. The basins are then annealed again before they are finally machined.
  • the production of the different variants of the pools for example ride pools, hi-hats, crash pools, china pools, splash pools and effect pools, therefore requires a particularly advantageous hot formability of the material, which is ensured by the alloy according to the invention.
  • different structural proportions can be used for the ö phase and for the hard particles can be set in a very wide range. In this way it is already possible on the alloy side to influence the sound of the cymbals.
  • Table 1 shows the chemical composition of alloy variant 1. This material has an Sn content of 7.35% by weight, an Si content of 0.74% by weight, an Al content of 0.34% by weight, a boron content of 0, 33% by weight as well as a P content of 0.015% by weight and the remainder copper.
  • Sn content 7.35% by weight
  • Si content 0.74% by weight
  • Al content 0.34% by weight
  • boron content 0 33% by weight
  • P content of 0.015% by weight and the remainder copper.
  • the structure of exemplary embodiment 1 is characterized by a very uniform, island-shaped distribution of a relatively small proportion of the ⁇ phase (1, approx. 20% by volume) and the hard particles 2 in the copper mixed crystal 3 ( Fig. 1 ).
  • the hardness of this type of alloy is 108 HB (Tab. 2).
  • Table 3 shows the chemical composition of a further alloy variant 2.
  • this material contains the other elements Si (0.80% by weight), Al (0.54% by weight), boron (0.24% by weight) .-%) and the remainder copper.
  • Si 0.80% by weight
  • Al 0.54% by weight
  • boron 0.24% by weight
  • ⁇ /b> Chemical composition of embodiment 2 (in% by weight) Cu Sn Si Al B. P 2 rest 15.09 0.80 0.54 0.24 0.027
  • the invention is characterized, inter alia, in that the structure in the as-cast state consists of increasing proportions of ⁇ -phase with increasing Sn content of the alloy, depending on the casting / cooling process.
  • the arrangement of this Sn-rich ⁇ -phase changes from a finely distributed island shape with an increase in the Sn content of the alloy into a dense network shape.
  • the ⁇ phase is present with a significantly higher content (up to 70% by volume).
  • This structure goes out Fig. 3 in 200 times and off Fig. 4 in 500x magnification.
  • the Sn-rich ⁇ -phase which is arranged in a network-like manner in the structure, is identified by the reference numeral 1 in each case.
  • the structural component of the copper mixed crystal is labeled with the reference number 3.
  • the uniform distribution of the island-shaped and / or network-like arranged ⁇ -phase in the structure of the tin-containing copper alloy according to the invention underlines the effect of the hard particles as crystallization nuclei for the formation of the ⁇ -phase.
  • One aspect of the invention relates to a method for producing strips, sheets, plates, bolts, wires, rods, tubes and profiles from the tin-containing copper alloy according to the invention with the aid of the permanent mold casting process or the continuous or semi-continuous continuous casting process.
  • the alloy according to the invention can also be subjected to further processing.
  • this enables the production of specific and often complex geometries.
  • the demand for an improvement of the complex operating properties of the materials, especially for components subject to wear and for structural and connecting elements in electronics / electrical engineering, is met, since it is a one in the corresponding machines, motors, gears, assemblies, constructions and systems strongly increasing stress on the system elements.
  • a significant improvement in the toughness properties and / or a significant increase in tensile strength R m , yield strength R p0.2 and hardness is achieved.
  • a further advantageous possibility of further processing the as-cast state or the hot-formed state or the annealed cast state or the annealed hot-formed state comprises carrying out at least one cold forming.
  • this process step in particular the material parameters R m , R p0.2 and the hardness are significantly increased. This is significant for applications in which there is mechanical stress and / or intensive abrasive and adhesive wear and tear on the components.
  • the spring properties of the components made of the alloy according to the invention are significantly improved as a result of cold forming.
  • At least one annealing treatment can be carried out in a temperature range from 200 to 880 ° C. with a duration of 10 minutes to 6 hours.
  • the resulting very fine-grained structure is an important prerequisite for producing the combination of properties of high strength and hardness and sufficient toughness of the material.
  • stress relief annealing can advantageously also be carried out in a temperature range from 200 to 650 ° C. with a duration of 0.5 to 6 hours.
  • further processing can be selected which includes at least one cold forming or the combination of at least one hot forming and at least one cold forming in connection with at least one annealing in a temperature range of 200 to 800 ° C with a duration of 10 minutes to 6 hours and to one recrystallized structure of the alloy according to the invention leads.
  • the fine-grain structure of the alloy adjusted in this way ensures a combination of high strength, high hardness and good toughness properties.
  • a stress-relieving treatment in the temperature range from 200 to 650 ° C with a duration of 0.5 to 6 hours can be carried out to reduce the internal stresses of the components.
  • the corresponding blocks or semi-finished products were characterized by an exceptionally smooth surface.
  • the hot-formed state of alloy variant 1 had sufficient cold formability.
  • the hot-rolled plates could be cold-rolled crack-free with a cold deformation ⁇ of approx. 85%.
  • the strips of alloy variant 1 were annealed at 680 ° C. for 3 hours after the first cold rolling. The strips were then cold-rolled with a cold deformation ⁇ of approx. 60%. To the At the end of production, the strips were thermally relaxed at various temperatures between 280 and 400 ° C for a period of 2 and 4 hours.
  • the characteristic values of the resulting material conditions are listed in Tab. 7.
  • FIG Fig. 2 The final state of the belt of embodiment 1 is in FIG Fig. 2 shown.
  • the fine-grain structure with the hard phases 2, which are embedded in the copper mixed crystal 3, can be seen.
  • the hard particles are coated with tin and / or the Sn-rich ⁇ phase.
  • the tapes of embodiment 2 of the invention were produced according to the production program shown in Table 9.
  • the hot-rolling of the chill casting formats took place at a temperature of 750 ° C with subsequent cooling in water. After chill casting and hot rolling, the corresponding blocks or semi-finished products were characterized by an exceptionally smooth surface.
  • the grain size and the hardness of the cold-rolled condition as well as the cold-rolled and annealed condition for the strips 2-A are shown in Table 10. Due to the dynamic recrystallization of the structure that took place during the hot rolling of the cast blocks, the structure is already in a uniform shape with a grain size of 20 to 25 ⁇ m after the first cold rolling.
  • the toughness properties can also be improved by means of an annealing treatment in the temperature range from 200 to 650 ° C.
  • the structure of embodiment 2 is shown after three hours of annealing at 500 ° C.
  • the ö-phase (dark colored) is distributed extremely evenly in the structure of the material. A further reduction in the proportion of the ⁇ phase is achieved by annealing at 600 ° C / 3h (Fig. 6).
  • the hard particles are more completely contained in the ⁇ -phase regions. This underlines the function of the hard particles as crystallization / precipitation nuclei, even during the thermomechanical processing of the alloy.
  • the structure of the strip 2-A which was finally heat-treated with the parameters 500 ° C / 3h + air and 600 ° C / 3h + air, is in FIGS. 5 and 6 shown.
  • the hard particles 2 are present, which are coated by tin and / or the Sn-rich ⁇ phase.
  • the copper mixed crystal 3 which consists of a low-tin ⁇ phase, can be seen.
  • the structure of the strip 2-A is coarse-grained ( Fig. 6 ).
  • the structure of exemplary embodiment 3 of the invention is progressively drawn in lines.
  • the line-like arrangement of the very high ⁇ component due to the high Sn content of the alloy leads to high hardness values close to 300 HV1.
  • the brittle character of the alloy increases.
  • the alloy according to the invention has excellent castability and hot formability over the entire range of Sn content from 4 to 23% Sn.
  • the cold formability is also at a very high level.
  • the ductility of the invention naturally deteriorates with increasing Sn content.

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Claims (19)

  1. Alliage de cuivre contenant de l'étain à haute résistance avec une excellente aptitude au formage à chaud et aptitude au formage à froid, une haute résistance à l'usure abrasive, à l'usure adhésive et à l'usure de contact ainsi qu'une résistance à la corrosion et une résistance à la relaxation des contraintes améliorées, consistant en (en % en poids):
    4,0 à 23,0 % de Sn,
    0,05 à 2,0 % de Si,
    0,01 à 1,0 % de Al,
    0,005 à 0,6 % de B,
    0,001 à 0,08 % de P,
    éventuellement jusqu'à un maximum de 2,0 % de Zn,
    éventuellement jusqu'à un maximum de 0,6 % de Fe,
    éventuellement jusqu'à un maximum de 0,5 % de Mg,
    éventuellement jusqu'à un maximum de 0,25 % de Pb,
    le reste de cuivre et d'impuretés inévitables,
    caractérisé en ce que
    - le rapport Si/B des teneurs en éléments des éléments silicium et bore est situé entre 0,3 et 10.
  2. Alliage de cuivre coulé contenant de l'étain à haute résistance avec une excellente aptitude au formage à chaud et aptitude au formage à froid, une haute résistance à l'usure abrasive, à l'usure adhésive et à l'usure de contact ainsi qu'une résistance à la corrosion et une résistance à la relaxation des contraintes améliorées, consistant en (en % en poids):
    4,0 à 23,0 % de Sn,
    0,05 à 2,0 % de Si,
    0,01 à 1,0 % de Al,
    0,005 à 0,6 % de B,
    0,001 à 0,08 % de P,
    éventuellement jusqu'à un maximum de 2,0 % de Zn,
    éventuellement jusqu'à un maximum de 0,6 % de Fe,
    éventuellement jusqu'à un maximum de 0,5 % de Mg,
    éventuellement jusqu'à un maximum de 0,25 % de Pb,
    le reste de cuivre et d'impuretés inévitables,
    caractérisé en ce que
    - le rapport Si/B des teneurs en éléments des éléments silicium et bore est situé entre 0,3 et 10;
    - les constituants structurels suivants sont présents dans l'alliage après la coulée:
    a) 1 jusqu'à 98 % en volume de phase δ riche en Sn (1),
    b) 1 jusqu'à 20% en volume de phases contenant Al et contenant B, de phases contenant Si et contenant B et/ou de composés d'addition et/ou de composés mixtes des deux phases (2),
    c) le reste de cristal mixte de cuivre, consistant en phase α pauvre en étain (3),
    où les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2) sont revêtus d'étain et/ou de la phase δ riche en Sn (1);
    - lors de la coulée, les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2), qui sont formés sous forme de borures d'aluminium et de borures de silicium et/ou de composés d'addition et/ou de composés mixtes des borures d'aluminium et des borures de silicium, représentent des germes pour une cristallisation uniforme pendant la solidification/le refroidissement de la masse fondue, de sorte que la phase δ riche en Sn (1) est uniformément répartie dans la structure sous forme d'îles et/ou de réseaux;
    - les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2), qui sont formés sous forme de borosilicates et/ou de borophosphosilicates et/ou d'oxyde d'aluminium-borosilicates et/ou d'oxyde d'aluminium-borophosphosilicates, jouent avec les silicates de phosphore et les oxydes d'aluminium le rôle d'un revêtement de protection contre l'usure et/ou de protection contre la corrosion sur les produits semi-finis et les pièces de l'alliage.
  3. Alliage de cuivre contenant de l'étain à haute résistance à l'état de traitement ultérieur avec une excellente aptitude au formage à chaud et aptitude au formage à froid, une haute résistance contre l'usure abrasive, l'usure adhésive et l'usure de contact, ainsi qu'une résistance à la corrosion et une résistance à la relaxation des contraintes améliorées, consistant en (en % en poids):
    4,0 à 23,0 % de Sn,
    0,05 à 2,0 % de Si,
    0,01 à 1,0 % de Al,
    0,005 à 0,6 % de B,
    0,001 à 0,08 % de P,
    éventuellement jusqu'à un maximum de 2,0 % de Zn,
    éventuellement jusqu'à un maximum de 0,6 % de Fe,
    éventuellement jusqu'à un maximum de 0,5 % de Mg,
    éventuellement jusqu'à un maximum de 0,25 % de Pb,
    le reste de cuivre et d'impuretés inévitables,
    caractérisé en ce que
    - le rapport Si/B des teneurs en éléments des éléments silicium et bore est situé entre 0,3 et 10;
    - après le traitement ultérieur de l'alliage par au moins un recuit ou par au moins un formage à chaud et/ou un formage à froid en plus d'au moins un recuit dans l'alliage, les constituants structurels suivants sont présents:
    a) jusqu'à 75 % en volume de phase δ riche en Sn (1),
    b) 1 jusqu'à 25 % en volume de phases contenant Al et contenant B, de phases contenant Si et contenant B et/ou de composés d'addition et/ou de composés mixtes des deux phases (2),
    c) le reste de cristal mixte de cuivre, consistant en phase α pauvre en étain (3), où les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2) sont revêtus d'étain et/ou de la phase δ riche en Sn (1);
    - les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2), qui sont formés sous forme de borures d'aluminium et de borures de silicium et/ou de composés d'addition et/ou de composés mixtes des borures d'aluminium et des borures de silicium, représentent des germes pour une recristallisation statique et dynamique de la structure pendant le traitement ultérieur de l'alliage, de sorte que l'établissement d'une structure uniforme et à grains fins a lieu;
    - les phases contenant Al et contenant B, les phases contenant Si et contenant B et/ou les composés d'addition et/ou les composés mixtes des deux phases (2), qui sont formés sous forme de borosilicates e/ou de borophosphosilicates et/ou d'oxyde d'aluminium-borosilicates et/ou d'oxyde d'aluminium-borophosphosilicates, jouent avec les silicates de phosphore et les oxydes d'aluminium le rôle de revêtement de protection contre l'usure et/ou de protection contre la corrosion sur les produits semi-finis et les pièces de l'alliage.
  4. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 3, caractérisé en ce que l'élément silicium est contenu à raison de 0,05 à 1,5 %.
  5. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 4, caractérisé en ce que l'élément silicium est contenu à raison de 0,5 à 1,5 %.
  6. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 5, caractérisé en ce que l'élément aluminium est contenu à raison de 0,1 à 0,8 %.
  7. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 6, caractérisé en ce que l'élément bore est contenu à raison de 0,01 à 0,6 %.
  8. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 7, caractérisé en ce que l'élément phosphore est contenu à raison de 0,001 à 0,05 %.
  9. Alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 8, caractérisé en ce que l'alliage est exempt de plomb à l'exception d'éventuelles impuretés inévitables.
  10. Procédé de production de produits finis et de pièces ayant une forme proche du produit fini à partir d'un alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 9 à l'aide du procédé de coulée en sable, du procédé de coulée en moule carapace, du procédé de coulée en cire perdue, du procédé de coulée en moule plein, du procédé de coulée sous pression ou du procédé lost-foam.
  11. Procédé de production de bandes, tôles, plaques, boulons, fils ronds, fils profilés, barres rondes, barres profilées, barres creuses, tubes et profilés à partir d'un alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 9 à l'aide du procédé de coulée en coquille ou du procédé de coulée continue continu ou semi-continu.
  12. Procédé selon la revendication 11, caractérisé en ce que le traitement ultérieur de l'état tel que coulé comprend la réalisation d'au moins un formage à chaud dans la plage de température de 600 à 880°C.
  13. Procédé selon l'une des revendications 10 à 12, caractérisé en ce qu'au moins un traitement de recuit est réalisé dans la plage de température de 200 à 880°C avec la durée de 10 minutes à 6 heures.
  14. Procédé selon l'une des revendications 11 à 13, caractérisé en ce que le traitement ultérieur de l'état tel que coulé ou de l'état formé à chaud ou de l'état tel que coulé recuit ou de l'état formé à chaud recuit comprend la réalisation d'au moins un formage à froid.
  15. Procédé selon la revendication 14, caractérisé en ce qu'au moins un traitement de recuit est réalisé dans la plage de température de 200 à 880°C avec la durée de 10 minutes à 6 heures.
  16. Procédé selon la revendication 14 ou 15, caractérisé en ce qu'un recuit de détente/recuit de précipitation est réalisé dans la plage de température de 200 à 650°C avec la durée de 0,5 à 6 heures.
  17. Utilisation de l'alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 9 pour des listels à rabattage de jeu et des listels de glissement, pour des bagues de friction et des disques de friction, pour des surfaces de paliers lisses dans des composants composites, pour des éléments de glissement et des éléments de guidage dans des moteurs à combustion interne, des soupapes, des turbocompresseurs, des engrenages, des installations de post-traitement des gaz d'échappement, des systèmes de leviers, des systèmes de freins et des systèmes d'articulations, des unités hydrauliques ou dans des machines et des installations de construction générale de machines.
  18. Utilisation de l'alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 9 pour des composants, des éléments de ligne, des éléments de guidage et des éléments de connexion en électronique/ électrotechnique.
  19. Utilisation de l'alliage de cuivre contenant de l'étain selon l'une des revendications 1 à 9 pour des objets métalliques dans l'élevage d'organismes vivant dans l'eau de mer, pour des instruments de frappe, pour des hélices, des ailes, des vis et moyeux de navires pour la construction navale, pour des boîtiers de pompes à eau, de pompes à huile et de pompes à carburant, pour des stators, des roues mobiles et des roues à aubes pour pompes et turbines à eau, pour des roues dentées, des roues à vis sans fin, des roues hélicoïdales ainsi que pour des écrous de pression et des écrous de broche ainsi que pour des tubes, des garnitures et des boulons de liaison dans l'industrie maritime et l'industrie chimique.
EP17706407.8A 2016-03-03 2017-02-10 Alliage de cuivre contenant de l'étain, procédé pour sa préparation ainsi que son utilisation Active EP3423604B1 (fr)

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DE102016002604.9A DE102016002604A1 (de) 2016-03-03 2016-03-03 Zinnhaltige Kupferlegierung, Verfahren zu deren Herstellung sowie deren Verwendung
PCT/EP2017/000189 WO2017148568A1 (fr) 2016-03-03 2017-02-10 Alliage de cuivre contenant de l'étain, procédé pour sa préparation ainsi que son utilisation

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CN111687407B (zh) * 2020-07-28 2022-07-26 鞍山大族激光技术有限公司 一种磷铜工件激光熔覆用铜粉及熔覆方法
DE102020004652B3 (de) * 2020-07-31 2021-12-16 Wieland-Werke Aktiengesellschaft Verfahren zur Herstellung eines Gleitelements
CN114262853A (zh) * 2021-11-23 2022-04-01 太仓市林源电线电缆有限公司 一种电工铜线的多重冷却低应力退火工艺

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CN108699631A (zh) 2018-10-23
WO2017148568A1 (fr) 2017-09-08
US20190062876A1 (en) 2019-02-28
DE102016002604A1 (de) 2017-09-07
CN108699631B (zh) 2020-08-04
JP2019511632A (ja) 2019-04-25
KR20180121889A (ko) 2018-11-09
MX2018010583A (es) 2018-11-09
EP3423604A1 (fr) 2019-01-09
JP6679742B2 (ja) 2020-04-15

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