EP1910582B1 - Verfahren zur herstellung einer kupferlegierung mit hoher dämpfungskapazität und deren verwendung - Google Patents

Verfahren zur herstellung einer kupferlegierung mit hoher dämpfungskapazität und deren verwendung Download PDF

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Publication number
EP1910582B1
EP1910582B1 EP06775757A EP06775757A EP1910582B1 EP 1910582 B1 EP1910582 B1 EP 1910582B1 EP 06775757 A EP06775757 A EP 06775757A EP 06775757 A EP06775757 A EP 06775757A EP 1910582 B1 EP1910582 B1 EP 1910582B1
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EP
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Prior art keywords
alloy
process according
temperature
temperatures
transformation
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Not-in-force
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EP06775757A
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German (de)
English (en)
French (fr)
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EP1910582A2 (de
Inventor
Hennadiy Zak
Sönke VOGELGESANG
Agnieszka Mielczarek
Babette Tonn
Werner Riehemann
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Technische Universitaet Clausthal
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Technische Universitaet Clausthal
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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 method for producing a copper alloy with adjusted to the application of the components alloy properties and specifically with targeted improved, or optimally adjusted mechanical damping, which is particularly suitable for mechanically, for example, by vibration, impact or shock, loaded components. Furthermore, the invention relates to the use of the alloy obtained by the method for reducing vibrations and noise attenuation of mechanically loaded components.
  • HIDAMETs Hlgh DAmping METals
  • high mechanical damping capacity is desirable for reducing vibration and noise reduction.
  • Such alloys are therefore particularly suitable for the manufacture of ship propellers and pump housings, as well as for use in vibrating machines and for preventing vibration disturbances in various precision apparatuses and electronic instruments.
  • the alloys are also suitable for use in various tools that are exposed to vibrations and / or shocks during operation, such as punches or dies in sheet metal forming or in lathes and milling machines.
  • HIDAMETs There are a variety of HIDAMETs known that can be used for noise damping and vibration absorption.
  • the fields of application of a large part of these materials, in particular of magnesium and magnesium alloys, are severely limited by their insufficient mechanical and corrosion properties.
  • HIDAMETs with martensitic phase transformations are of particular importance in the art for achieving high attenuation properties. Alloys with martensitic phase transformations have a different atomic arrangement in the solid state at high temperatures than at low temperatures.
  • the high temperature phase is referred to as "austenite” and the low temperature phase as “martensite”.
  • austenite The transformation of austenite into martensite takes place on cooling of the material from the austenitic state and begins at the martensite start temperature MS.
  • the martensitic transformation is completed when the martensite finish temperature MF is reached.
  • Ni-Ti alloy (“Nitinol”), Cu-Zn-Al alloys (“Proteus”) and Mn-Cu alloys (“Sonoston”).
  • Ni-Ti alloys must be produced consuming under vacuum and are also very expensive due to the alloying elements involved.
  • Cu-Zn-Al alloys are much cheaper.
  • the limited corrosion resistance and the tendency to brittle fracture behavior are significant disadvantages of these alloys.
  • they are extremely severe in both the austenitic and the martensitic state to aging.
  • Mn-Cu alloys have been specially developed for the manufacture of ship propellers. Due to the relatively wide solidification interval of about 130 ° C, these alloys are prone to hot cracking. In addition, aging effects also occur here, so that a significant decrease in the damping effect occurs already at room temperature after storage for about 1000 hours.
  • the patent US Pat. No. 3,868,279 discloses high-damping Cu-Mn-Al alloys and a way to improve their damping properties by heat treatment.
  • These ternary alloys contain 32-42% by weight of Mn, 2-4% by weight of Al and the remainder of Cu, the Mn content preferably being 40% and the Al content preferably being 2-3%.
  • These alloys are cold rolled and heat treated at temperatures between 649 ° C and 760 ° C, quenched in water, then aged at 204 ° C to 482 ° C for 1.5 to 24 hours and cooled in air. It is described a significant improvement in damping properties with less brittleness compared to the prior art Heusler alloys.
  • a technically interesting material alternative to the HIDAMETs described above are Cu-Al-Mn shape memory alloys. These materials also exhibit a thermoelastic martensite transformation.
  • the patent US 4,146,392 describes Cu-Al-Mn shape memory alloys containing in addition to the main constituent copper as alloying constituents 4.6 to 13 wt .-% manganese and 8.6 to 12.8 wt .-% aluminum and have a good resistance to aging. These are alloys whose austenite-martensite transformation takes place at temperatures below 0 ° C. and whose shape memory effect is exploited, for example to produce pipe connection elements.
  • the alloys proposed for this purpose contain, in addition to copper and aluminum, for example, an element from the group of zinc, silicon, manganese and iron.
  • the invention therefore an object of the invention to provide heavy-duty and corrosion-resistant HIDAMETs with a precisely adjustable even in the decisive for the intended application temperature range high damping capacity and a method for their production.
  • the object of the invention is achieved by the method according to claim 1 and the use according to claim 13.
  • Steps c) and d) may be repeated as many times as necessary until the desired adaptation of the transformation temperatures or intervals is achieved.
  • the alloys obtained by the process according to the invention are otherwise produced by conventional melting and casting processes. Apart from cast alloy, the alloy can also be used as wrought alloy. The alloy can be cold or hot formed.
  • the alloys described herein are particularly advantageous for all applications where a high mechanical damping capacity is required, i. especially for mechanically loaded components, devices or housings that are subject to vibrations, impacts or shocks.
  • the alloys differ from Sonoston in significantly higher aluminum 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 cast-technological properties of the alloy due to the reduction in the solidification interval.
  • dense, oxide and warm crack-free casts can be produced with unit weights of several tons without quality problems.
  • the proportions of the alloy components are usually varied, for. B. as described in more detail below. It has been found that the mechanical damping capacity, which frequently fluctuates greatly with variation of the composition , can be optimized and set to higher values with the aid of a targeted fine tuning of the contents of the individual alloy components than if only the martensitic region were preferred for better reproducible damping properties. as is usual in the prior art.
  • the martensit austenitic transformation temperatures or the associated intervals M s to M F and / or A s to A F adapted to a predetermined operating or operating temperature which will occur in the intended use of the alloy in a "component".
  • component is intended to cover all conceivable practical applications and include both individual parts, such as more complex composite components, housings, machines and the like.
  • Both the operating temperature and the working temperature can be medium temperatures, ie average values from a working or application area.
  • both transition temperature intervals, the martensitic and the austenitic may be used to set to one or more different operating temperature ranges. The adjustment is made by varying the weight proportions of the above alloying ingredients during the melting of the alloy.
  • nickel, iron, cobalt, zinc, silicon, vanadium, niobium, molybdenum, chromium, tungsten, beryllium, lithium, yttrium, cerium, scandium, calcium, titanium, phosphorus, zirconium, boron, nitrogen, carbon it is possible to specially adapt the properties of the alloy obtained by the process to the particular application.
  • addition of nickel or silicon increases corrosion resistance and strength properties.
  • the elements iron, vanadium, niobium, molybdenum, chromium, tungsten, yttrium, cerium, scandium, calcium, titanium, zirconium, boron are important for achieving grain refining.
  • 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 in both austenitic and martensitic states is increased by the addition of cobalt.
  • Beryllium and phosphorus protect the melt from oxidation.
  • the alloy therefore preferably contains between 1 and 4% by weight of nickel.
  • a preferred embodiment of the alloy contains between 11.6 and 12% by weight, preferably about 11.8% by weight of aluminum.
  • manganese contents between 8 and 10 wt .-% are preferred in the alloy.
  • the alloy may further preferably contain between 0.01 and 1% by weight of cobalt.
  • the structure of the cast alloy is characterized by relatively large cast grains and is preferably grain-fined to achieve optimum mechanical properties. become. Boron additions between 0.001 and 0.05% by weight and / or chromium additions between 0.01 and 0.8% by weight and / or iron additions of 2 to 4% by weight are particularly effective for this purpose.
  • the grain refining can be carried out by adding rare earths up to 0.3% by weight.
  • the alloy may further contain between 2 and 6% zinc.
  • the alloys may preferably have MS temperatures> 0 ° C, without the invention being limited thereto.
  • the invention provides a significant improvement in the damping properties, since only by the invention, the optimal adjustment of these properties while taking into account other desired properties is possible.
  • the method according to the invention makes it possible to adapt the transformation temperatures in the material to the respective conditions of use such that the specific damping capacity of the alloys according to the invention reaches up to 80% and more at the intended application temperature.
  • a particularly composed copper alloy contains as alloying components more than 4% by weight of manganese, more than 10% by weight of aluminum, 0.01 to 0.8 wt .-% chromium and individually or in total 0 to 18% by weight of one or more 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, but each element does not exceed 6% and contains 100 wt .-% copper.
  • a selected copper alloy which is suitable in particular for mechanically loaded components with specifically improved mechanical damping, contains as alloy constituents > 4 to 12% by weight of manganese, > 10 to 14% by weight of aluminum, 0.01 to 0.8 wt .-% chromium and individually or in total 0 to 18% by weight of one or more 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, but each element not more than 6% and ad 100% by weight of copper.
  • the copper alloy may preferably contain between 1 and 4 wt% nickel.
  • the copper alloy may preferably contain between 11.6 and 12% by weight, more preferably about 11.8% by weight of aluminum.
  • the copper alloy may preferably contain between 8 and 10% by weight of manganese.
  • the copper alloy may preferably contain between 2 and 4% by weight of iron and / or between 0.001 and 0.05% by weight of boron.
  • the copper alloy may preferably contain between 0.01 and 1 wt% cobalt.
  • the copper alloy may preferably contain between 0.01 and 0.3 wt% of rare earths.
  • the copper alloy may furthermore preferably contain between 2 and 6% by weight of zinc.
  • This abovementioned copper alloy can be obtained according to the invention by adapting the martensit-austenitic transformation temperatures or the associated intervals MS to MF and / or AS to AF to a predetermined operating or operating temperature of the component, as described above.
  • Affinity to oxygen is preferable to adding aluminum to lower the transition temperatures to an addition of manganese.
  • the maximum values for the specific damping capacity occur in the alloy according to the invention during cooling from the austenite state in the range between M s and M F and when heating from the Martensitschreib between A s and A F.
  • the temperature in the middle of the martensitic or austenitic phase transition interval should be as close as possible to the operating temperature of components made from the alloy of the invention. It is therefore possible with the invention to produce alloys for specific predetermined service or operating temperatures or temperature ranges, which are then particularly suitable for certain applications and components.
  • the exact adjustment of the transformation temperatures is made with a sample taken during the melting process which allows an express control of the transformation temperatures for the liquid alloy.
  • a sample for the express control it is preferable to use a cast wire drawn from the melt by means of a quartz tube in which a negative pressure is generated.
  • the determination of the transformation temperatures can be carried out on this sample, depending on the expected application either in the casting state or after the heat treatment by known experimental methods for the detection of Phasentiber réellen.
  • the transformation temperature on the sample may be by calorimetry, dilatometry, electrical conductivity measurement, light microscopy, or acoustic emission measurement.
  • the martensitic transformation can also be initiated in a defined temperature range via externally applied voltages.
  • the transformation temperatures in the material increase linearly with the load. This increase in the transformation temperatures must already be considered in the production of components made from the alloy according to the invention, if mechanical stresses are to be expected there.
  • the damping maximum is also considerably influenced by the microstructure of the alloy, with larger grains leading to better damping properties.
  • the grain size of the alloy can be adjusted so that for each specific application, an optimal compromise between the damping capacity and the mechanical properties is achieved.
  • an improvement of the damping properties can be achieved by a heat treatment.
  • a heat treatment As particularly effective has an annealing at temperatures of 650 ° C to 950 ° C with subsequent cooling or quenching (quenching) in liquid or gaseous media such.
  • quenching quenching
  • 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 transition temperatures can be reduced according to the invention by an additional aging of the quenched alloy at a temperature of 150 ° C to 250 ° C. Expediently, such outsourcing takes 5 to 120 minutes.
  • a martensitic structure can be produced in the surface layer according to a further feature of the invention by laser remelting.
  • the surface layer takes over the damping role, without the entire component must be subjected to a costly heat treatment.
  • the transformation temperatures of the alloy during melting by the express control are adjusted so that, taking into account the cooling conditions in the laser remelting, the transition temperatures in the surface layer correspond to the application temperature of the component.
  • the alloys obtained by the process according to the invention can be used particularly advantageously for reducing vibrations for noise damping on mechanically loaded components, in particular in ship propellers, machine housings, in particular pump housings, generator housings, vibrating machines, precision apparatus, electronic instruments, tools which, during operation, oscillate and / or or are exposed to blows or generate them, in particular stamps, dies, machine hammers, turning and milling tools.
  • the sample is a cast wire having a length of 10 to 150 mm (preferably 15 to 100 mm) and a cross-sectional area of 0.2 to 7 mm 2 , preferably 0.7 to 3.2 mm 2 . This is pulled out of the melt with the help of a quartz tube, in which a negative pressure is generated. This sample can be used directly and very quickly with known detection methods. In a preferred method also used here, the acoustic emission is tracked over a temperature profile.
  • Fig. 1 Formation of specific damping capacity of the alloy of the example taken for a heating and cooling cycle
  • FIG. 1 shows a measurement diagram that have been taken to the example described above.
  • the specific damping capacity is plotted in% above the temperature in ° C.
  • the temperatures were passed through in a heating and cooling cycle from below zero to 200 ° C and back.
  • the example alloy in the austenitic interval much higher attenuation can be achieved than in the martensitic, so that the frequently occurring in the art restriction to martensitic structures must lead to significant disadvantages for the alloy properties.
  • the example alloy achieves its maximum damping properties at a temperature of 120 ° C and thus successfully fulfills the stated task.
  • the achievable damping is over 70%.
EP06775757A 2005-07-27 2006-07-27 Verfahren zur herstellung einer kupferlegierung mit hoher dämpfungskapazität und deren verwendung Not-in-force EP1910582B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
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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EP1910582A2 EP1910582A2 (de) 2008-04-16
EP1910582B1 true EP1910582B1 (de) 2012-09-05

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

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CN104250714A (zh) * 2014-08-26 2014-12-31 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

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DE102007009996B4 (de) 2007-03-01 2014-03-27 Minebea Co., Ltd. Elektromotor
WO2011046055A1 (ja) * 2009-10-14 2011-04-21 独立行政法人科学技術振興機構 Fe基形状記憶合金及びその製造方法
KR101231919B1 (ko) 2010-12-14 2013-02-08 한욱희 자동차 와이퍼 벤딩 다이용 동합금 소재
CN102212714B (zh) * 2011-05-11 2012-11-28 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
CN102296206B (zh) * 2011-09-08 2012-11-07 中南大学 一种高强耐磨变形铝青铜合金
CN102808105B (zh) * 2012-08-24 2014-11-26 朱育盼 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
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
CN108277535B (zh) * 2018-01-10 2019-07-23 厦门大学 一种铜铝锰基单晶合金材料
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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CN104250714A (zh) * 2014-08-26 2014-12-31 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
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

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US20080298999A1 (en) 2008-12-04
JP2009503250A (ja) 2009-01-29
EP1910582A2 (de) 2008-04-16
DE102005035709A1 (de) 2007-02-15
DE112006002577A5 (de) 2008-06-26
WO2007012320A3 (de) 2007-05-31
WO2007012320A2 (de) 2007-02-01

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