US20080298999A1 - Method for Producing a Copper Alloy Having a High Damping Capacity - Google Patents

Method for Producing a Copper Alloy Having a High Damping Capacity Download PDF

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Publication number
US20080298999A1
US20080298999A1 US11/995,842 US99584206A US2008298999A1 US 20080298999 A1 US20080298999 A1 US 20080298999A1 US 99584206 A US99584206 A US 99584206A US 2008298999 A1 US2008298999 A1 US 2008298999A1
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United States
Prior art keywords
alloy
weight
copper
temperature
copper alloy
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Abandoned
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US11/995,842
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Inventor
Hennadiy Zak
Soenke Vogelgesang
Agniezka Mielczarek
Babette Tonn
Werner Riehemann
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Technische Universitaet Clausthal
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Assigned to TECHNISCHE UNIVERSITAET CLAUSTHAL reassignment TECHNISCHE UNIVERSITAET CLAUSTHAL ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: RIEHEMANN, WERNER, VOGELGESANG, SOENKE, TONN, BABETTE, ZAK, HENNADIY, MIELCZAREK, AGNIEZKA
Publication of US20080298999A1 publication Critical patent/US20080298999A1/en
Abandoned legal-status Critical Current

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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
    • C22C9/01—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
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/05—Alloys based on copper with manganese as the next major constituent

Definitions

  • the invention relates to a process for producing a copper alloy which is particularly suitable for components which are mechanically stressed, for example by vibration, shock or impact and has alloy properties which are matched to the intended use of the components, especially specifically improved or optimally set mechanical damping.
  • the invention further relates to such an alloy having a particular composition and possible uses of the alloys obtained by the process.
  • HIDAMETs HIDAMETs
  • a high mechanical damping capacity is desirable, for example, for reduction of vibrations and for noise damping.
  • Such alloys are therefore particularly suitable for producing ships' propellers and pump housings and for use in vibrating machines and for preventing malfunctions caused by vibration in the case of various precision apparatuses and electronic instruments.
  • the alloys have not only a high wear resistance but are suitable for use in various tools which are subjected to vibrations and/or impacts during operation, for example punches or dies in the shaping of sheetmetal or in lathes and milling machines.
  • HIDAMETs which display martensitic phase transformations are of particular importance in the prior art for achieving good damping properties.
  • Alloys which display martensitic phase transformations have a different arrangement of atoms in the solid state at high temperatures than at low temperatures.
  • the hightemperature phase is referred to as “austenite” and the low-temperature phase is referred to as “martensite”.
  • the transformation of austenite into martensite occurs on cooling the material from the austenitic state and commences at the martensite start temperature M S .
  • the martensitic transformation is concluded on reaching the martensite finish temperature M F .
  • Ni—Ti alloys (“Nitinol”), Cu—Zn—Al alloys (“Proteus”) and Mn—Cu alloys (“Sonoston”).
  • Ni—Ti alloys have to be produced in a complicated fashion under reduced pressure and are also very expensive because of the participating alloying elements.
  • Cu—Zn—Al alloys are significantly cheaper.
  • the limited corrosion resistance and the tendency to display brittle fracture are significant disadvantages of these alloys. In addition, they are extraordinarily prone to aging both in the austenitic state and in the martensitic state.
  • Mn—Cu alloys were developed specifically for producing ships' propellers. Due to the relatively wide solidification range of about 130° C., these alloys display a strong tendency to hot crack formation. In addition, aging effects also occur here, so that the damping effect is significantly reduced after storage for about 1000 hours at room temperature.
  • U.S. Pat. No. 3,868,279 discloses high-damping Cu—Mn—Al alloys and a possible way of improving their damping properties by means of heat treatment.
  • These ternary alloys comprise 32-42% by weight of Mn, from 2-4% by weight of Al and Cu as balance, with the Mn content preferably being 40% and the Al content preferably being 2-3%.
  • These alloys are cold rolled and subjected to heat treatment at temperatures in the range from 649° C. to 760° C., quenched in water, subsequently aged at from 204° C. to 482° C. for from 1.5 to 24 hours and cooled in air.
  • a significant improvement in the damping properties combined with reduced brittleness compared to the previously known Heusler alloys is described.
  • DE 2055755 discloses a process for producing articles composed of copper-based alloys which are able to change their shape when the temperature changes.
  • the alloys proposed for this purpose comprise copper and aluminum together with, for example, an additional element from the group consisting of zinc, silicon, manganese and iron.
  • the object of the invention is achieved by a process for producing a copper alloy having specifically improved mechanical damping, in particular for mechanically stressed components, which is characterized by the following steps:
  • Steps c) and d) can be repeated as often as necessary until the desired matching of the transformation temperatures or ranges has been achieved.
  • composition of the alloy is selected from among the constituents:
  • the alloys obtained by the process of the invention are otherwise produced by conventional melting and casting processes.
  • the alloy can be used not only as a casting alloy but also as a forging alloy.
  • the alloy can be shaped cold or hot.
  • the alloys described here are particularly advantageous for all applications in which a high mechanical damping capacity is important, i.e. in particular for mechanically stressed components, instruments or housings which are subjected to vibrations, impacts or shocks.
  • the alloys differ from Sonoston in their considerably higher aluminum contents and significantly lower manganese contents.
  • the high aluminum content improves the strength of the material according to the invention and at the same time increases its resistance to abrasion, erosion and cavitation.
  • the reduced manganese concentration has a positive effect on the casting properties of the alloy because it reduces the solidification range. Dense, oxide-free and hot-crackfree castings can thus be produced without quality problems even for piece weights of several tons.
  • the proportions of the components of the alloy are usually varied, e.g. as described in more detail below. It has been found that the mechanical damping capacity which frequently alters greatly when the composition is varied can be optimized by means of a targeted fine tuning of the contents of the individual components of the alloy and set to higher values than if only the martensitic range were to be preferred for more readily reproducible damping properties, as is otherwise customary in the prior art.
  • the martensite-austenite transformation temperatures or the associated ranges M S to M F and/or A S to A F are matched to a predetermined use or working temperature which will occur in the intended use of the alloy in a “component”.
  • a high internal friction is also set as a result.
  • the term “component” is intended to cover all conceivable practical use possibilities and include both individual parts and more complex multipart components, housings, machines and the like.
  • Both the use temperature and the working temperature can be average temperatures, i.e. means of a working range or use range.
  • both transformation temperature ranges viz. the martensitic range and the austenitic range, can be used for matching to one relatively large working temperature range or two different working temperature ranges. Matching is achieved by variation of the proportions by weight of the abovementioned constituents of the alloy during melting of the alloy.
  • the properties of the alloy obtained by the process can be specifically matched to the respective intended use by means of the elements nickel, iron, cobalt, zinc, silicon, vanadium, niobium, molybdenum, chromium, tungsten, beryllium, lithium, yttrium, cerium, scandium, calcium, titanium, phosphorus, zirconium, boron, nitrogen, carbon.
  • nickel or silicon increases the corrosion resistance and strength properties.
  • the elements iron, vanadium, niobium, molybdenum, chromium, tungsten, yttrium, cerium, scandium, calcium, titanium, zirconium, boron are of importance for achieving a fine-grade structure.
  • Nitrogen and carbon together with transition elements improve the mechanical properties of the alloy obtained according to the invention.
  • the aging resistance of the alloy both in the austenitic state and the martensitic state is increased by addition of cobalt.
  • Beryllium and phosphorus protect the melt against oxidation.
  • various combinations of the alloying elements enable a more or less strong influence to be exerted on the transformation temperatures of the alloy of the invention in order to optimally match the requirement profile for a specific application.
  • the alloy therefore preferably contains from 1 to 4% by weight of nickel.
  • a preferred embodiment of the alloy contains from 11.6 to 12% by weight, preferably about 11.8% by weight, of aluminum.
  • manganese contents in the range from 8 to 10% by weight in the alloy are preferred.
  • the alloy can also preferably contain from 0.01 to 1% by weight of cobalt.
  • the microstructure of the cast alloy has relatively large cast grains and the grains are preferably made finer in order to achieve the optimal mechanical properties.
  • Boron additions in the range from 0.001 to 0.05% by weight and/or chromium additions in the range from 0.01 to 0.8% by weight and/or iron additions of from 2 to 4% by weight are particularly effective for this purpose.
  • grain refinement can also be effected by addition of rare earths in an amount of up to 0.3% by weight.
  • the alloy can also contain from 2 to 6% of zinc.
  • the alloys preferably have M S temperatures of >0° C., without the invention being restricted thereto.
  • the invention gives a significant improvement in the damping properties since optimal setting of these properties while at the same time maintaining other desired properties has been made possible for the first time by the invention.
  • the process of the invention enables the transformation temperatures in the material to be matched to the respective use conditions so that the specific damping capacity of the alloys of the invention at the intended use temperature is up to 80% and more.
  • the invention also encompasses a copper alloy which has a particular composition and comprises, as constituents of the alloy,
  • This novel alloy for mechanically stressed components can additionally have the further specifications as indicated above and can likewise be obtained by matching the martensite-austenite transformation temperatures or the associated ranges M S to M F and/or A S to A F to a predetermined use or working temperature of the component, as described above.
  • the maximum values for the specific damping capacity occur when the alloy is cooled from the austenitic state to a temperature in the range from M S to M F and when the alloy is heated from the martensitic state to a temperature in the range from A S to A F .
  • the temperature in the middle of the martensitic or austenitic range of the phase transformation should therefore be very close to the use temperature of components composed of the alloy of the invention.
  • the invention therefore makes it possible to produce alloys for specific predetermined use or working temperatures or temperature ranges, which are then particularly suitable for particular applications and components.
  • the precise setting of the transformation temperatures is carried out using a sample which is taken during the melting process and allows express monitoring of the transformation temperatures for the liquid alloy.
  • sample for express monitoring preference is given to using a cast wire which is drawn from the melt with the aid of a fused silica tube in which a subatmospheric pressure is generated.
  • the transformation temperatures can be determined on this sample either in the cast state or after heat treatment, depending on the intended use, by means of known experimental methods for detecting phase transformations.
  • the transformation temperature of the sample is preferably determined by calorimetry, dilatometry, measurement of the electrical conductivity, optical microscopy or measurement of the acoustic emission.
  • a direct correction of the chemical composition of the melt is made, preferably by means of copper or aluminum as described above.
  • the process of the invention thus makes it possible to set the transformation temperatures in the material so that the alloy achieves the maximum possible damping capacity at the desired use temperature. Efficient matching of the material to the respective use conditions is therefore basically ensured.
  • the martensitic transformation can also be induced in a defined temperature range by means of externally applied stresses.
  • the transformation temperatures in the material increase linearly with the stress. This increase in the transformation temperatures has to be taken into account in the production of components from the alloy of the invention if mechanical stresses are to be expected there.
  • the damping maximum is also influenced to a considerable extent by the microstructure of the alloy, with larger grains leading to better damping properties.
  • the grain size of the alloy can be set by means of suitable alloying measures so that an optimal compromise between the damping capacity and the mechanical properties is achieved for each specific application.
  • an improvement in the damping properties can be achieved by means of heat treatment. Heating at temperatures of from 650° C. to 950° C. with subsequent cooling or quenching in liquid or gaseous media, e.g. air, liquid nitrogen, water, a salt bath or oil, has been found to be particularly effective.
  • the temperature of the quenching medium should preferably be above the M S temperature in order to avoid uncontrollable shifts in the transformation temperatures in the material.
  • the aging sensitivity of the transformation temperatures can, according to the invention, be reduced by means of additional heat treatment of the quenched alloy at a temperature of from 150° C. to 250° C. The duration of such a heat treatment is advantageously from 5 to 120 minutes.
  • a martensitic microstructure can, according to a further aspect of the invention, be produced in the outer layer by laser remelting.
  • the outer layer takes on the damping role without the entire component having to be subjected to costly heat treatment.
  • the transformation temperatures of the alloy are set during melting by means of express monitoring so that, taking into account the cooling conditions during laser remelting, the transformation temperatures in the outer layer correspond to the use temperature of the component.
  • the alloys obtained by the process of the invention can be used particularly advantageously for reducing vibrations and for noise damping on mechanically stressed components, especially for ships, propellers, machine housings, in particular pump housings, generator housings, vibrating machines, precision apparatuses, electronic instruments, tools which are subjected to vibrations and/or impacts during operation or produce these, in particular for punches, dies, machine hammers, lathe tools and milling tools.
  • Noise-damping compressor housings or various hydraulic components can be produced using an alloy which displays its maximum damping properties at a temperature of about 120° C.
  • FIG. 1 Development of the specific damping capacity of the alloy from the example, recorded for one heating and cooling cycle
  • FIG. 1 shows a curve recorded for the above-described example.
  • the specific damping capacity in % is plotted against the temperature in 0° C.
  • the temperatures were raised from below zero to 200° C. and brought back again in a heating and cooling cycle.
  • significantly higher damping is achieved in the austenitic range than in the martensitic range for the illustrative alloy, so that the restriction to martensitic structures which is frequently applied in the prior art has to lead to significant disadvantages in terms of the alloy properties.
  • the illustrative alloy attains its maximum damping properties at a temperature of 120° C. and thus successfully achieves the object set.
  • the damping which can be achieved is above 70%.
US11/995,842 2005-07-27 2006-07-27 Method for Producing a Copper Alloy Having a High Damping Capacity Abandoned US20080298999A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102005035709.1 2005-07-27
DE102005035709A DE102005035709A1 (de) 2005-07-27 2005-07-27 Kupferlegierung mit hoher Dämpfungskapazität und Verfahren zu ihrer Herstellung
PCT/DE2006/001305 WO2007012320A2 (de) 2005-07-27 2006-07-27 Verfahren zur herstellung einer kupferlegierung mit hoher dämpfungskapazität

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US (1) US20080298999A1 (ru)
EP (1) EP1910582B1 (ru)
JP (1) JP2009503250A (ru)
DE (2) DE102005035709A1 (ru)
WO (1) WO2007012320A2 (ru)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102212714A (zh) * 2011-05-11 2011-10-12 上海振嘉合金材料厂 一种高精度锰铜电阻合金窄扁带及其制造方法
CN102296206A (zh) * 2011-09-08 2011-12-28 中南大学 一种高强耐磨变形铝青铜合金
CN102808105A (zh) * 2012-08-24 2012-12-05 李伟 一种形状记忆铜合金的制备方法
KR101231919B1 (ko) 2010-12-14 2013-02-08 한욱희 자동차 와이퍼 벤딩 다이용 동합금 소재
CN103421981A (zh) * 2013-08-08 2013-12-04 常熟市东方特种金属材料厂 高阻尼形状记忆合金
US8815027B2 (en) 2009-10-14 2014-08-26 Japan Science And Technology Agency Fe-based shape memory alloy and its production method
CN108277535A (zh) * 2018-01-10 2018-07-13 厦门大学 一种铜铝锰基单晶合金材料
EP3910086A1 (de) * 2020-05-14 2021-11-17 Wieland-Werke AG Kupfer-mangan-aluminium-eisen-knetlegierung

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DE102007009996B4 (de) 2007-03-01 2014-03-27 Minebea Co., Ltd. Elektromotor
CN104250714B (zh) * 2014-08-26 2016-04-20 无棣向上机械设计服务有限公司 一种低密度抗冲击金属材料及其制作方法
EP3241919B1 (de) 2016-05-04 2020-01-08 Wieland-Werke AG Kupfer-aluminium-mangan-legierung und deren verwendung
DE102017200645A1 (de) 2017-01-17 2017-12-28 Carl Zeiss Smt Gmbh Optische Anordnung, insbesondere Lithographiesystem
CN109266887B (zh) * 2018-12-03 2019-12-10 河北工业大学 一种高阻尼铜基形状记忆合金的制备方法
DE102019105453A1 (de) * 2019-03-04 2020-09-10 Kme Mansfeld Gmbh Verfahren zum kontinuierlichen Herstellen eines Kupferlegierungsprodukts
CN111057886B (zh) * 2019-10-29 2021-06-22 宁夏中色新材料有限公司 一种铍铜铸轧辊套的制备方法和铍铜铸轧辊套
CN110952045A (zh) * 2019-12-23 2020-04-03 安徽旭晶粉体新材料科技有限公司 一种高性能的合金铜粉及其制备方法

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US20030079814A1 (en) * 2001-10-25 2003-05-01 Harchekar Vijay Rajaram Cu-Zu-A1(6%) shape memory alloy with low martensitic temperature and a process for its manufacture

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8815027B2 (en) 2009-10-14 2014-08-26 Japan Science And Technology Agency Fe-based shape memory alloy and its production method
KR101231919B1 (ko) 2010-12-14 2013-02-08 한욱희 자동차 와이퍼 벤딩 다이용 동합금 소재
CN102212714A (zh) * 2011-05-11 2011-10-12 上海振嘉合金材料厂 一种高精度锰铜电阻合金窄扁带及其制造方法
CN102296206A (zh) * 2011-09-08 2011-12-28 中南大学 一种高强耐磨变形铝青铜合金
CN102808105A (zh) * 2012-08-24 2012-12-05 李伟 一种形状记忆铜合金的制备方法
CN103421981A (zh) * 2013-08-08 2013-12-04 常熟市东方特种金属材料厂 高阻尼形状记忆合金
CN108277535A (zh) * 2018-01-10 2018-07-13 厦门大学 一种铜铝锰基单晶合金材料
EP3910086A1 (de) * 2020-05-14 2021-11-17 Wieland-Werke AG Kupfer-mangan-aluminium-eisen-knetlegierung

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Publication number Publication date
DE112006002577A5 (de) 2008-06-26
EP1910582A2 (de) 2008-04-16
EP1910582B1 (de) 2012-09-05
JP2009503250A (ja) 2009-01-29
DE102005035709A1 (de) 2007-02-15
WO2007012320A3 (de) 2007-05-31
WO2007012320A2 (de) 2007-02-01

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