EP1930452B1 - Metal matrix material based on shape-memory alloy powders, production method thereof and use of same - Google Patents

Metal matrix material based on shape-memory alloy powders, production method thereof and use of same Download PDF

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Publication number
EP1930452B1
EP1930452B1 EP06807938.3A EP06807938A EP1930452B1 EP 1930452 B1 EP1930452 B1 EP 1930452B1 EP 06807938 A EP06807938 A EP 06807938A EP 1930452 B1 EP1930452 B1 EP 1930452B1
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EP
European Patent Office
Prior art keywords
composite material
particles
metal matrix
shape
memory alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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EP06807938.3A
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German (de)
English (en)
French (fr)
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EP1930452A1 (en
Inventor
Jose Maria SAN JUAN NUÑEZ
Maria Luisa NÓ SÁNCHEZ
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Euskal Herriko Unibertsitatea
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Euskal Herriko Unibertsitatea
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/14—Casting in, on, or around objects which form part of the product the objects being filamentary or particulate in form
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0425—Copper-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the invention relates to the area of Material Science and Technology as far as the design and production of the materials are concerned, and to the area of Physical Technology with regard to the properties of high damping.
  • the sectors of industrial activity in which the invention can apply are: domestic appliances and domotics, machine-tools and machinery in general, electronic packaging, transport including aeronautics, aerospace, construction.
  • SMA Shape Memory Alloys
  • beta high temperature phase
  • martensite low temperature phase
  • the interphases of martensite are mobile both during the transformation and in the martensite phase, and under the effect of a vibration or external mechanical stress they are liable to undergo movement, absorbing mechanical energy and giving rise to the powerful damping displayed by SMAs [2].
  • Copper-based SMAs are known to display a coefficient of damping higher than those of Ti-Ni which are the SMAs that are commercially used in practically all applications.
  • U.S. Patent No. 6,346,132 discloses a composite material containing a metallic second phase dispersed in a metallic matrix material.
  • the metallic second phase makes up 5 to 60 volume % of the overall composite material.
  • the matrix material is preferably an aluminium alloy.
  • this patent does not disclose directly and unambiguously a metal matrix comprising metals of melting point below 330°C or alloys of said metals with a solidifying point below 330°C.
  • the technical problem that is raised and which has led to the present invention is to achieve a material with a high coefficient of damping tan( ⁇ ), whose maximum can be adjusted to a particular temperature range, depending on the application it is intended for.
  • the elastic modulus E is required to be as high as possible in order to optimise the relation tan( ⁇ ) ⁇ E.
  • the present invention relates to a metal matrix composite material characterised in that it is based on particles of shape-memory alloy powder, having a copper base with a concentration of between 45% and 70% by volume in relation to the total volume of the material, said powder particles being supported by a metal matrix.
  • the copper base is present in the material at a concentration of between 50% and 60% by volume in relation to the total volume of the composite material.
  • the inventive material displays a thermoelastic martensitic transformation at between -150°C and +250°C.
  • the copper base is selected from among Cu-Al-Ni, Cu-Zn-Al and Cu-Al-Mn.
  • Said metal matrix of metals or alloys surrounds the powder particles and acts as a binder for the composite material.
  • the metal matrix comprises:
  • Said metal, or metals (or their alloys), of low melting point must be ductile at the temperature of the adjusted maximum damping.
  • metals that can constitute the metal matrix can be selected, among others, In, Sn, Pb, Cd, Tl and their alloys.
  • the alloy powder particles will be able to have the same single concentration of copper base, or the composite material will be able to include particles of different concentrations of base copper.
  • the composite material will be able to include particles of different concentrations of base copper.
  • the percentage of particles with a different concentration of copper base can be equal to or less than 15% in relation to the entire composite material.
  • particles of different composition will also be able to be included in the composite material, being able to be rigid, metallic or ceramic, and having the sole purpose of increasing the modulus of the composite material.
  • Said powder particles of different composition can be present in the material in a percentage equal to or less than 15% of the composite material. Moreover, these particles can be chosen from among Rhenium, Tungsten, Molybdenum, Silicon Carbide and Boron Carbide.
  • the present invention furthermore relates to a method for obtaining a metal matrix composite material as defined above, which comprises:
  • the shape-memory alloy powder particles can be obtained by means of spraying with gas or by any other method permitting powder particles to be obtained which display the thermoelastic martensite transformation proper to shape-memory alloys.
  • Said method can furthermore comprise a stage of adjusting the temperature range of the damping maximum of the composite material via the direct or inverse martensite transformation temperatures of the powder particles, varying the composition of the constituent elements of the shape-memory alloy.
  • said method can comprise the inclusion in the composite material of particles of different concentrations of copper base, which can be included in the composite material by means of heat treatment.
  • said method can comprise the inclusion in the composite material of particles with a concentration gradient in the composite material by means of mechanical alloying.
  • the method as claimed comprises:
  • the infiltration is carried out under pressure which can be achieved by means of centrifugation or by means of applying gas pressure to the melt.
  • the metal matrix comprises one or more metals with a melting point above 330°C, or alloys of those metals
  • the properties of the martensite transformation of the shape-memory alloy powder particles will have to be preserved, due to which said method can be a powder metallurgy method, which comprises:
  • the compaction can be carried out using sinterisation with uniaxial stressing at a temperature below 300°C or the compaction can also be done by means of previous encapsulating in vacuo and subsequent isostatic compacting at high pressure at a temperature below 300°C.
  • This method can also possibly be used in the case of metal matrices with lower melting point, such as those mentioned above in the embodiment described in the method.
  • the method in which the matrix comprises metals with a melting point higher than 330°C the method can alternatively be an infiltration method at high temperature, which can comprise:
  • the choice of the metal matrix will serve to optimise the binder properties of the composite material, as will optimise the relation tan( ⁇ ) ⁇ E, and will be chosen according to the type of SMA used and the range of temperatures at which the composite material is going to find itself under service conditions in the various applications.
  • the shape-memory alloy powder particles contribute a high coefficient of damping for the composite material, owing to the movement of the martensite interphases, especially in the proximity of the martensite transformation temperature (direct or inverse).
  • the matrix permits absorption of the deformation which the particles undergo when the martensite interphases move, whether this be in the martensite phase or when undergoing the transformation induced by temperature or stress. In this way, the matrix absorbs the deformation of the particles preventing the composite material from degrading.
  • the matrix also contributes to the continual damping background and generates an amplifying effect for the damping of the particles.
  • the temperature range of the damping maximum can be adjusted between -150°C and +250°C, via the martensite transformation temperatures (direct or inverse) of the powder particles, which are in turn controlled by means of the composition of the elements constituting the alloy with shape-memory.
  • the present invention also refers to the use of the composite material defined earlier for the absorption of vibrations.
  • Said vibrations can be acoustic or mechanical.
  • the solution contributed by the present invention to the problem raised is therefore a novel concept of composite material based on shape-memory alloy (SMA) powder particles with copper base, as the main damping elements with a percentage ⁇ 40% embedded in a ductile metal matrix, of low melting point.
  • SMA shape-memory alloy
  • copper base SMA powders are in response to the fact that said alloys display a coefficient of damping higher than Titanium-Nickel base SMAs. Furthermore, via the control of the composition of these powder particles, the temperature of the damping maximum can be adjusted. The low melting point metal matrix, as well as providing support for the particles, also generates an amplifying effect on the damping, never before described.
  • An example of embodiment of the composite materials that have been described is the following: Alloy powders of Cu-Al-Ni have been used with a concentration by weight: 13.1% Al, 3.1% Ni, 83.8% Cu. The powders were produced by means of spraying by gas. And powders have been used that were passed through a sieve of sizes between 25 and 50 microns.
  • Indium of purity 99.99% was used as matrix metal.
  • the powders introduced into a teflon mould were degasified at 130°C for 6 hours in a vacuum of 0.01 mbar.
  • the infiltration was performed at 190°C, by means of applying a helium gas pressure of 3 bars on the melt.
  • the composite material contained 60% by volume of Cu-Al-Ni particles and 40% indium.
  • the damping coefficient tan( ⁇ ) has been measured in torsion with a mechanical electroscopy equipment which permits one to work at different frequencies and according to temperature, since, as is well known, the coefficient of damping of a material depends on these two parameters.
  • the composite material displays two damping maxima at 65°C and 100°C corresponding to the direct and inverse martensite transformation respectively. Stated below are the values of the coefficient of damping for different frequencies:

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
EP06807938.3A 2005-08-31 2006-08-30 Metal matrix material based on shape-memory alloy powders, production method thereof and use of same Active EP1930452B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
ES200502129A ES2276605B1 (es) 2005-08-31 2005-08-31 Un material compuesto de matriz metalica basado en polvos de aleacion con memoria de forma, su procedimiento de obtencion y uso.
PCT/ES2006/000493 WO2007026039A1 (es) 2005-08-31 2006-08-30 Un material compuesto de matriz metalica basado en polvos de aleaci n con memoria de forma/ su procedimiento de obtenci n y uso

Publications (2)

Publication Number Publication Date
EP1930452A1 EP1930452A1 (en) 2008-06-11
EP1930452B1 true EP1930452B1 (en) 2019-01-09

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP06807938.3A Active EP1930452B1 (en) 2005-08-31 2006-08-30 Metal matrix material based on shape-memory alloy powders, production method thereof and use of same

Country Status (5)

Country Link
US (1) US20090123329A1 (enExample)
EP (1) EP1930452B1 (enExample)
JP (1) JP2009506217A (enExample)
ES (2) ES2276605B1 (enExample)
WO (1) WO2007026039A1 (enExample)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20130216815A1 (en) * 2010-08-25 2013-08-22 Torxx Group Inc Composite materials and methods and apparatus for making same
CN102011038B (zh) * 2010-12-15 2012-02-29 河北师范大学 Mn50Ni50-xAlx高温铁磁形状记忆合金材料及其制备方法
JP5403707B2 (ja) * 2011-12-27 2014-01-29 福田金属箔粉工業株式会社 Ｃｕ系溶浸用粉末
CA2769075A1 (en) * 2012-02-24 2013-08-24 Torxx Group Inc. Highly filled particulate composite materials and methods and apparatus for making same
KR101988014B1 (ko) 2012-04-18 2019-06-13 삼성디스플레이 주식회사 어레이 기판의 제조 방법 및 이에 사용되는 제조 장치
CN102719695A (zh) * 2012-06-25 2012-10-10 镇江忆诺唯记忆合金有限公司 一种用粉末冶金法制备的CuAlMn记忆合金
CN111745162B (zh) * 2019-03-26 2022-04-05 中国科学院金属研究所 具有三维互穿网络结构的形状记忆合金增强镁基复合材料及其制备方法
CN115341119A (zh) * 2022-07-19 2022-11-15 华南理工大学 一种4d打印的铜基形状记忆合金粉末及其应用
CN116479285B (zh) * 2023-04-06 2025-03-21 武汉理工大学 一种具有超大压缩弹性应变多孔Cu-Al-Mn基合金的制备方法

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JPS5429809A (en) * 1977-08-10 1979-03-06 Hitachi Ltd Preparation of damping sintered material
DE3068396D1 (en) * 1980-03-03 1984-08-09 Bbc Brown Boveri & Cie Process for the production of a copper, zinc and aluminium base memory alloy by powder metallurgy technique
JPS5993848A (ja) * 1982-11-22 1984-05-30 Toshiba Corp 防振合金
JPH1017959A (ja) * 1996-07-03 1998-01-20 Furukawa Electric Co Ltd:The 複合材及びその製造方法
US6346132B1 (en) * 1997-09-18 2002-02-12 Daimlerchrysler Ag High-strength, high-damping metal material and method of making the same
DE19741019C2 (de) * 1997-09-18 2000-09-28 Daimler Chrysler Ag Strukturwerkstoff und Verfahren zu dessen Herstellung
US6796408B2 (en) * 2002-09-13 2004-09-28 The Boeing Company Method for vibration damping using superelastic alloys
US20060284313A1 (en) * 2005-06-15 2006-12-21 Yongqian Wang Low stress chip attachment with shape memory materials

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Also Published As

Publication number Publication date
ES2725078T3 (es) 2019-09-19
US20090123329A1 (en) 2009-05-14
ES2276605A1 (es) 2007-06-16
ES2276605B1 (es) 2008-05-16
EP1930452A1 (en) 2008-06-11
JP2009506217A (ja) 2009-02-12
WO2007026039A1 (es) 2007-03-08

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