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

• a metal matrix composite material based on alloy powders with shape memory its method of obtaining and using
• the invention corresponds to the area of Materials Science and Technology, in regard to the design and elaboration of materials, as well as to the area of Physical Technology in regard to high damping properties.
• the sectors of industrial activity in which the invention can be applied are: household appliances and home automation, machine tools and machinery in general, electronic packaging, transportation including aeronautics, aerospace, construction.
• the materials with the highest damping coefficient are polymeric materials, due to their viscoelastic behavior.
• polymers generally have a low elastic modulus and this is inconvenient for the design of materials with high damping for structural applications.
• the merit index for the structural damping design is the product of the elastic modulus (or stiffness) E, by the damping coefficient tg ( ⁇ ), so it is about optimizing the ratio tg ( ⁇ ) E That is why various types of high-damping metal materials have been developed, also known as HIDAMETS (High Damping Metals), since metals have an elastic modulus far superior to polymers.
• SUBSTITUTE SHEET (RULE 26) Memory Alloys ") [1]. These alloys undergo a thermoelastic (reversible) martensitic transformation between their high temperature phase, called beta, and their low temperature phase, called martensite, which can be induced by cooling or by applying mechanical stress. The interfaces of martensite are mobile both during the transformation, and in the martensite phase, and under the effect of a vibration or external mechanical tension they are capable of moving, absorbing mechanical energy and giving rise to the strong damping presented by SMAs [2]. It is known that copper-based SMAs have a higher damping coefficient than those of Ti-Ni, which are SMAs that are commercially used in virtually all applications.
• the technical problem that arises and has led to the present invention is to achieve a material with a high damping coefficient tg ( ⁇ ), whose maximum can be adjusted to a particular temperature range, depending on the application to which it is intended .
• the elastic module E is required to be as high as possible, in order to optimize the ratio tg ( ⁇ ) • E.
• SMA dust particles constitute the majority element with a percentage between 45% and 70%, being responsible for the strong damping of the composite material.
• the dust particles are copper-based SMA and have their own martensitic transformation in an adjustable temperature range.
• the temperature range of the maximum damping of the composite material is very wide (> 50 ° C) and can be adjusted by controlling the composition of the SMA dust particles. *) .
• the matrix must be a metal matrix with a low melting point, and that is ductile at the martensitic transformation temperature of the SMA particles. *) .- The matrix contributes to the damping fund and generates an amplifying effect of the damping of the particles, never described so far.
• the composite materials thus obtained can have a tg ( ⁇ ) • E ratio, which can be optimized over a wide temperature range, better than any other material currently specified.
• the present invention relates to a metal matrix composite material characterized in that the damping element is based on alloy particles with shape memory, copper base with a concentration between 45% and 70% by volume with respect to
• the copper base is present in the material in a concentration between 50% and 60% by volume with respect to the total volume of the composite material.
• the material of the invention has a thermoelastic martensitic transformation between -150 0 C and +250 0 C.
• the copper base is selected from Cu-Al-Ni, Cu-Zn-Al and Cu-Al-Mn .
• Said metal matrix of metals or alloys surrounds the dust particles and serves as a binder to the composite material.
• the metal matrix may comprise, according to embodiments of the invention:
• Said metal, or metals, (or their alloys) of low melting point must be ductile at the maximum set damping temperature.
• the low melting metals that can constitute the metal matrix among others, In, Sn, Pb, Cd, Tl, and their alloys can be selected.
• the metal matrix can be selected from: - one or more metals of melting point above 330 0 C, or
• the alloy dust particles may be Zn or Mg.
• the alloy dust particles may be any suitable metals in this case.
• SUBSTITUTE SHEET (RULE 26) have the same and unique concentration of copper base, or particles of different concentrations of copper base may be included in the composite.
• particles with a copper-based concentration gradient may be included so that the martensitic transformation has a more extended temperature range, and thus obtain a maximum of temperature widened damping.
• the percentage of particles with different concentration of copper base may be equal to or less than 15% with respect to the total composite material.
• Said dust particles of different composition may be present in the material in a percentage equal to or less than 15% of composite material.
• these particles may be selected from Rhenium, Tungsten, Molybdenum, Silicon Carbide and Boron Carbide.
• the present invention further relates to a process for obtaining a metal matrix composite material as defined above comprising: - preparing the shape memory alloy powder particles, and
• the dust particles of the shape memory alloy can be obtained by gas atomization, or by any other method that allows obtaining
• SUBSTITUTE SHEET (RULE 26) dust particles presenting the thermoelastic martensitic transformation typical of shape memory alloys.
• Said process can also comprise a step of adjusting the temperature range of the maximum damping of the composite material through the temperatures of direct or inverse martensitic transformation of the dust particles, the composition of the constituent elements of the alloy with memory of varying shape.
• said process may comprise the inclusion in the composite material • of particles of different concentration of copper base, which may be included in the composite material by heat treatment.
• said process may comprise the inclusion in the composite material of particles with a concentration gradient in the composite material by mechanical alloy.
• the matrix metal comprises metals of melting point below 330 0 C, or alloys of these metals with lower solidus temperature of 330 ° C, said process comprising
• the infiltration is carried out at a pressure that can be achieved by centrifugation or by applying a gas pressure on the melt.
• the metal matrix comprises one or more metals of melting point above 330 0 C, or alloys of these metals have to preserve the properties of the martensitic transformation of the powder particles memory alloy form, so that said procedure may be a powder metallurgy procedure, comprising:
• the compaction can be carried out by sintering with uniaxial tension at a temperature below 300 0 C, or the compaction can also be carried out by pre-encapsulation under vacuum and subsequent isostatic compaction at high pressure at a temperature below 300 0 C Eventually, this method may also be used in the case of metal matrices with a lower melting point, such as those mentioned above in the previously described embodiment of the process.
• the procedure may be an infiltration method at high temperature, which may comprise: -preparing particles of copper powder base,
• SUBSTITUTE SHEET (RULE 26) temper the composite material in a rapid cooling medium.
• Said rapid cooling medium may be water.
• the choice of the metal matrix will be used to optimize the binding properties of the composite material, as well as the ratio tg ( ⁇ ) • E, and will be chosen based on the type of SiVLA used and the temperature range in which the composite material will be found in service conditions in the various applications.
• the shape memory alloy dust particles provide a high damping coefficient to the composite material, due to the movement of the martensite interfaces, especially in proximity to the martensitic transformation temperature (direct or inverse) .
• the matrix allows to absorb the deformation that the particles experience when the martensite interfaces move, either in the martensitic phase, or when they undergo temperature-induced or voltage-induced transformation. In this way, the matrix absorbs the deformation of the particles preventing the composite material from degrading.
• the matrix in addition to supporting the particles in the composite material, also contributes to the continuous damping background and generates an amplifying effect of the damping of the particles.
• the temperature range of the maximum damping can be adjusted between -150 0 C and +250 0 C, through the martensitic transformation temperatures (direct or inverse) of the dust particles, which in turn is controlled by the composition
• the present invention also relates to the use of the composite material defined above for vibration absorption. These vibrations can be acoustic or mechanical.
• the potential industrial applications of the present invention can be very numerous, and in general all those where high vibration damping is required. Below are some examples of applications that the materials of the present invention may have:
• the concept itself is innovative, since in traditional composite materials, it is the matrix that acts as a damping element and the particles or fibers are added to increase the modulus.
• the use of copper-based SMA powders responds to the fact that these alloys have a damping coefficient greater than Titanium-Nickel based SMAs.
• the maximum damping temperature can be adjusted.
• the low melting point metal matrix in addition to supporting the particles, generates an amplifying damping effect, never described so far.
• Cu-Al-Ni alloy powders with a concentration by weight have been used: 13.1% Al, 3.1% Ni, 83.8% Cu.
• the powders were produced by gas atomization. And sieved powders with sizes between 25 and 50 microns have been used.
• the powders introduced into a teflon mold were degasified at 130 0 C for 6 hours under a vacuum of 0.01 mbar.
• Infiltration was carried out at 190 0 C, by applying a pressure on the melt, helium gas at 3 bar.
• the composite material contained 60% by volume of Cu-Al-Ni particles and 40% indium.
• the damping coefficient tg ( ⁇ ) has been measured in torsion with mechanical spectroscopy equipment that allows working at different frequencies and depending on the temperature, since as it is well known the damping coefficient of a material depends on these two parameters .
• the composite material has two damping maximums at 65 ° C and 100 0 C corresponding to the direct and inverse martensitic transformation respectively.
• the values of the damping coefficient for different frequencies are indicated below:
• tg ( ⁇ )> 0.01 between -100 0 C and + 125 ° C, with a maximum of tg ( ⁇ )> 0.05
• tg ( ⁇ )> 0.09 between - 100 0 C and + 125 ° C, with a maximum of tg ( ⁇ )> 0.6.

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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)

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• 2005
  • 2005-08-31 ES ES200502129A patent/ES2276605B1/es not_active Expired - Fee Related
• 2006
  • 2006-08-30 ES ES06807938T patent/ES2725078T3/es active Active
  • 2006-08-30 WO PCT/ES2006/000493 patent/WO2007026039A1/es not_active Ceased
  • 2006-08-30 US US11/991,262 patent/US20090123329A1/en not_active Abandoned
  • 2006-08-30 EP EP06807938.3A patent/EP1930452B1/en active Active
  • 2006-08-30 JP JP2008528542A patent/JP2009506217A/ja active Pending

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