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WO2014207776A1 - Procédé permettant de produire des composites à matrice aluminium au moyen d'une infiltration sans pression - Google Patents

Procédé permettant de produire des composites à matrice aluminium au moyen d'une infiltration sans pression Download PDF

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Publication number
WO2014207776A1
WO2014207776A1 PCT/IT2014/000168 IT2014000168W WO2014207776A1 WO 2014207776 A1 WO2014207776 A1 WO 2014207776A1 IT 2014000168 W IT2014000168 W IT 2014000168W WO 2014207776 A1 WO2014207776 A1 WO 2014207776A1
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Prior art keywords
aluminum
preform
infiltration
reinforcement
matrix
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English (en)
Inventor
Xiang Chen
Matteo Pavese
Claudio Francesco BADINI
Paolo Fino
Sara Biamino
Wenshu YANG
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Politecnico di Torino
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Politecnico di Torino
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • 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
    • C22C1/1005—Pretreatment of the non-metallic additives
    • C22C1/1015—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform
    • 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
    • C22C1/1005—Pretreatment of the non-metallic additives
    • C22C1/1015—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform
    • C22C1/1021—Pretreatment of the non-metallic additives by preparing or treating a non-metallic additive preform the preform being ceramic
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
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    • C22C1/10—Alloys containing non-metals
    • C22C1/1036—Alloys containing non-metals starting from a melt
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    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/062—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on B4C
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/065—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on SiC
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/12—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on oxides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/16—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on nitrides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C22C32/0057—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on B4C
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
    • C22C32/0063—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on SiC
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
    • C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides

Definitions

  • the present invention refers to a method for producing aluminum matrix composites through pressureless infiltration.
  • Aluminum matrix composites possess high specific stiffness and specific strength, good high temperature properties, fine fatigue and wear resistance, good damping capacity and low thermal expansion coefficient. As any other composite, they can combine specific mechanical and physical properties to satisfy requirements of application. Accordingly, aluminum matrix composites have become one of the most common and important metal matrix composites .
  • Aluminum matrix composites are usually fabricated by the process of squeeze casting, powder metallurgy, pressure infiltration, stirring casting and pressureless infiltration or spontaneous infiltration.
  • pressureless infiltration processing has a greater potential for industry application for its simple process, low cost and since it has no limitation on the size or shape of the products.
  • the main shortcoming for this processing is its application scope.
  • the application of pressureless infiltration is highly reliable on the wettability between reinforcement material and molten aluminum or aluminum alloys, while usually the wettability is relatively poor for the common used ceramic reinforcement (such as alumina) and molten matrix aluminum or aluminum alloys.
  • US-A-5509555 discloses a method of producing an article by pressureless reactive infiltration.
  • a porous preform containing at least carbon can be infiltrated by a liquid infiltrant alloys containing at least two elements among Al and Si or Cu and Si. Wetting is achieved along with the infiltration process thanks to the formation of silicon carbide.
  • the component of the preform it must contain carbon
  • the infiltrating alloys Al-Si or Cu-Si
  • the temperature required in US-A-5509555 is relatively high (900 °C-1800 °C) , usually higher than 900 °C, resulting in a high cost of production.
  • EP-A-0291441 describes a method of making a aluminum matrix composite by spontaneous infiltration of a permeable mass of ceramic filler material with a molten aluminum.
  • matrix aluminum alloy contains at least about 1 weight percent magnesium
  • balance non-oxidizing gas is in the range from 700 °C to 1200 °C
  • the aluminum matrix composites produced typically contain aluminum nitride in the aluminum matrix as a discontinuous phase, which is formed during the infiltration thanks to the reaction between the aluminum matrix (also thanks to the presence of magnesium) and the nitrogen atmosphere, and is believed to have a positive effect on the spontaneous infiltration.
  • the required control of atmosphere and the component of matrix alloy make the process complex, increase the cost of production and limit the application (only a magnesium-containing aluminum alloy can serve as matrix) .
  • EP-A-0115742 discloses a composite structural electrolytic aluminum-production cell component with the structure of a ceramic preformed matrix infiltrated by aluminum. It provides one way to render the non-wettable material (such as alumina) wettable by molten aluminum through pre-coating a wetting agent on its surface.
  • the wetting agent can be chosen among lithium, magnesium, calcium, titanium, chromium, iron, cobalt, nickel, zirconium or hafnium and the diborides of titanium, zirconium, hafnium and niobium.
  • the pre- coating process would greatly increase the cost of equipment and production. Besides, the required temperature is usually too high (with Ni coating, 1200 °C for 12 hours) so that it is not suitable for commercial application.
  • EP-A0368784 discloses a method of fabricating metal matrix composites by spontaneously infiltrating the filler material or preform with molten matrix metal, where the infiltration is believed to be induced by the communication between infiltrating atmosphere and filler material, or preform or matrix metal, which would supply some infiltration enhancer or infiltration enhancer precursor at the interface between matrix and filler.
  • the present invention significantly broaden the application. The point is at the presence of nitrogen together with an infiltration enhancer precursor such as magnesium/strontium or at the presence of oxygen together with zinc/calcium, the matrix aluminum melt can spontaneously infiltrate the filler. Similar to EP-A-0291441, wetting occurs along with the infiltration during forming infiltration enhancer.
  • the required control of atmosphere and the component of matrix alloy make the process complex, increase the cost of production and limit the application.
  • EP-A-1178127 discloses a method for producing metal-based composite by pressureless infiltration without control of atmosphere.
  • infiltration-accelerating metal magnesium
  • reinforcing filler silicon carbide
  • the aluminum container is sealed and melted in a matrix metal melt.
  • After infiltration, by solidifying the matrix metal melt and portion of the matrix metal a composite is produced.
  • sealed aluminum container with residual air inside generates a pressure at high temperature which contributes to the initial infiltration, the reaction products of magnesium and air improve the wetting and contribute to the final infiltration.
  • Purpose of the present invention is solving the above prior art problems; to simplify the process, flexibly control the reinforcement percentage and further extend the application scope of pressureless infiltration technology, a new approach of fabricating aluminum matrix composites is provided in the current invention, wherein most of reinforcement materials like oxides (alumina, silica, etc) , carbides (SiC, TiC, B 4 C, etc) , borides (TiB 2 , A1B, gB 2 ) , nitrides (A1N, TiN, Si 3 N 4 ) can be pressureless infiltrated by molten aluminum or aluminum alloys at temperature range of 700 °C-1500 °C, with mixing them with sufficient amount of aluminum or aluminum alloys powder, in a protective environment such as Nitrogen, Argon or Vacuum atmosphere.
  • reinforcement materials like oxides (alumina, silica, etc) , carbides (SiC, TiC, B 4 C, etc) , borides (TiB 2 , A1B, g
  • FIG. 1 is a schematic, side sectional view of a crucible in which Example 1 of the method of the present invention can be carried out;
  • FIG. 2 is a schematic, side sectional view of a crucible in which Example 2 of the method of the present invention can be carried out;
  • FIG. 3 is a schematic diagram of the main steps of the method according to the present invention.
  • a permeable mass or preform comprising at least one kind of reinforcement and aluminum or aluminum alloys powder can be infiltrated by molten aluminum or aluminum alloy in a protective environment without extra pressure.
  • the reinforcement materials comprise oxides (alumina, silica, etc.), carbides (SiC, Tie, B 4 C, etc.), borides (TiB 2 , AlB, MgB 2 , etc.), nitrides (AlN, TiN, Si 3 N 4 , etc.).
  • Said aluminum powder can be the same as a matrix metal or different from a matrix metal as component.
  • a sufficient amount of aluminum is required for a good infiltration and the amount depends on the properties of the reinforcement, the aluminum powder and the formed preform, and also on the infiltration temperature, since the dimension of the reinforcement and aluminum powder and the porosity of the preform have an evident influence on the infiltration. Generally speaking, a higher temperature, a larger reinforcement dimension and a lower preform porosity would have a positive influence on the infiltration.
  • the derived composites can be taken out directly from a molten aluminum bath at a relatively low temperature (about 680 °C) , and cooled with air, or they can be cooled down along with the molten aluminum bath with a furnace, and then be cut out from the solidified remains.
  • the inventive method for producing aluminum matrix composites through pressureless infiltration comprises the steps of:
  • the step of preparing as pre-wettability comprises the substeps of:
  • step of mechanically mixing is alternatively performed as:
  • a coating was prepared in a refractory crucible (alumina) with a layer of fine alumina powder, and it was put inside the preform and two 6061 aluminum alloy masses with one of the mass on the top, another one on the bottom ( Figure 1) .
  • the crucible was put into a furnace and the furnace was ventilated with inert Argon to form a protective atmosphere.
  • the furnace was heated with a rate of 300-400 °C/h for 3-4 hours until it reached 1200 °C, holding the temperature for 2 hours. After infiltration, the furnace was cooled down to room temperature, then the application of argon gas was stopped and the crucible was taken out, finally cutting out the derived composites from the remains inside the crucible.
  • Al 2 O3 P /6061Al composites by pressureless infiltration were obtained.
  • titanium diboride powder with dimension of 2-10 microns and -325 mesh 2024 aluminum alloy powder were mixed by stirring in a solution of butanol at room temperature for 2 hours.
  • the weight ratio of the three components (TiB 2 : 2024-A1: Butanol) was 1: 1: 2.
  • the suspension was left standing for 30 minutes until sedimentation occurred.
  • the liquid top layer was removed and the remains were stirred at 80 °C for another 30 minutes, till all liquid was removed.
  • the mixture powders were subjected to cold isostatic pressing to get a preform with a pressure of 150-200 MPa; the porosity of the preform was about 25%-30%.
  • the preform and matrix 2024 aluminum alloys were arranged into refractory crucibles as shown in Figure 2.
  • the crucible was put into a furnace and the furnace was ventilated with nitrogen gas to form a protective atmosphere.
  • the furnace was heated at the infiltration temperature of 700 °C with a heating rate of 300- 400 °C for about 2 hours, holding the temperature at 700 °C for other 2 hours to generate the infiltration.
  • the furnace was cooled down to 680 °C in 30 minutes, and the temperature was held for other 30 minutes. Then the application of nitrogen gas was stopped, fetching the derived composites and cooling it down in air.
  • TiB 2P /2024 Al composites by pressureless infiltration were obtained.
  • titanium carbide powder with particle size of 2-10 microns and -325 mesh 7075 aluminum alloys powder were mixed by stirring in a solution of ethanol.
  • Their weight ratio (TiC : 7075 : ethanol) was 19: 1: 10; the stirring process lasted 2 hours at room temperature to insure a good mixing of the mixture powder.
  • the suspension was left standing for 30 minutes for sedimentation, then the top liquid layer was removed and the stirring process was continued for another 30 minutes at 80 °C to insure the complete evaporation of residual ethanol.
  • a process of cold isostatic pressing was applied to prepare the preform.
  • the obtained preform had a porosity of around 35%-40%.
  • the preform stuck in the middle of two 7075 aluminum alloys bulks was arranged inside of a refractory crucible and placed in a high temperature furnace. Vacuum atmosphere was required and a heating rate of 600 °C/hour was started when the vacuum degree was under 0.01 pascal. The temperature was held at 1100 °C for 2 hours, and the furnace was substantially cooled down to room temperature. Finally, TiC p /7075 Al composites were obtained by cutting off the connected aluminum.
  • Example 4 UF10 silicon carbide powder and -325 mesh Al- Sil0% powder with weight ratio of 5:1 were mixed by low speed ball milling along with butanol for about 2 hours. The suspension was taken out into a beaker for sedimentation leaving it stand for 30 minutes. After having removed the top butanol layer, the mixture sediment was heated and stirred at 80 °C for other 30 minutes to evaporate the remaining butanol, till the mixture was completely dry. Isostatic pressing was applied to the well mixed powder under a 200 MPa - 250 Pa pressure at ambient temperature and the porosity of the obtained preform was about 34%-38%.
  • the preform was put in the middle of two Al-lOSi alloys bulks, arranging them inside a refractory crucible and then heating them to 1000 °C with a high temperature furnace in an argon protective atmosphere.
  • the heating rate was about 300-400 °C/h and after holding at 1000 °C for 2 hours, the furnace was cooled down to ambient temperature.
  • the derived composites were cut out from the solidified remains and SiC p /Al(Si) was obtained.
  • -325 mesh silicon powder and -325 mesh aluminum powder with a weight ratio of 1:10 were added into a mixture solvent of ethanol, butanol and fish oil.
  • the suspension was mixed with some polyvinyl butyral (PVB) binder and polyethylene glycol (PEG) through low speed ball milling for 12 hours.
  • PVB polyvinyl butyral
  • PEG polyethylene glycol
  • Chopped silicon carbide fibers with 12 micron in diameter and 10mm in length were gradually added into the stirred slurry from a ball milling jar.
  • the slurry was kept stirred for other 6 hours, then gas bubbles were removed from the slurry by reducing the air pressure.
  • Tapes were made on a Tape Caster instrument with the final slurry.
  • the air-dried tapes were firstly wetted with a mixture solvent of polyvinyl alcohol (PVA) , ethanol and butanol; and then stacked to form a bulk.
  • PVA polyvinyl alcohol
  • the preform was obtained by degreasing the bulk in an oven at a temperature of 500 °C protected by inert argon gas.
  • Two bulks of Al-lOSi alloys were sandwiched with the prepared preform and arranged into a refractory crucible inside an oven protected by inert argon gas.
  • the oven temperature was raised at a rate of about 300-400 °C/h for 2-3 hours, and was held at 900 °C for 2 hours until infiltration completed.
  • the oven was cooled down to room temperature, the connected aluminum was separated, and SiC Sf /Al-10Si composites were obtained.
  • a silicon carbide whisker with dimension of 1.5 micron in diameter and approximately 18 micron in length was used as reinforcement.
  • the silicon carbide whisker was stirred with -325 mesh Al-lOSi aluminum alloys for 2 hours to make them well mixed; their weight ratio was 10:1.
  • the preform was prepared from the mixture through isostatic cold pressing with a pressure of 200-250 MPa and the preform porosity was around 25%.
  • the preform was infiltrated similarly to what is described in Example 5, except that the infiltrating temperature was 850 °C.
  • the furnace was cooled down to room temperature, the remains were taken out in the crucible, the connected aluminum was separated, and SiC w /Al-10Si composites were obtained.
  • a titanium nitride powder of a 2-10 micron size was mixed with 2219 aluminum alloys with a weight ratio of 3:2 through stirring for 2 hours. After being thoroughly mixed, the powder mixture was cold pressed to form a preform through isostatic pressing under a 200-250 MPa pressure, and the preform porosity was around 30-35%.
  • the preform was infiltrated similarly as Eample 2, except that the infiltration temperature was 750 °C and the matrix alloys were 2219 aluminum alloy. After infiltration, the furnace was cooled down to 680 °C in 30 minutes, holding the temperature for other 30 minutes. Then, the application of nitrogen gas was stopped, the derived composites were fetched and cooled down in air. TiN p /2219 Al composites by pressureless infiltration were obtained.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Ceramic Engineering (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)

Abstract

La présente invention se rapporte à la production de composites à matrice aluminium au moyen d'une infiltration sans pression, une préforme, composée de mélanges d'au moins un type de matériaux de renforcement et de poudre d'aluminium ou d'alliage d'aluminium, étant spontanément infiltrée par de l'aluminium liquide de matrice ou des alliages d'aluminium dans un environnement protecteur à une température comprise entre 700 °C et 1 500 °C.
PCT/IT2014/000168 2013-06-27 2014-06-24 Procédé permettant de produire des composites à matrice aluminium au moyen d'une infiltration sans pression Ceased WO2014207776A1 (fr)

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IT000531A ITTO20130531A1 (it) 2013-06-27 2013-06-27 Metodo per la fabbricazione di compositi a matrice di alluminio tramite infiltrazione senza pressione
ITTO2013A000531 2013-06-27

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WO2014207776A1 true WO2014207776A1 (fr) 2014-12-31

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CN105761773A (zh) * 2016-03-07 2016-07-13 镇江纽科利核能新材料科技有限公司 乏燃料贮运用中子吸收材料的制备方法
CN107353008A (zh) * 2017-06-20 2017-11-17 西安交通大学 一种层状金属‑陶瓷复合材料零件的制备方法
CN110983092A (zh) * 2019-12-12 2020-04-10 中国科学院长春光学精密机械与物理研究所 一种无压浸渗炉和制备颗粒增强铝基复合材料的方法
CN117026029A (zh) * 2023-08-09 2023-11-10 仲恺农业工程学院 一种高强高阻尼铝锌双金属合金及其制备方法
CN117444180A (zh) * 2023-10-31 2024-01-26 北方工业大学 一种残余铝料易分离的无压浸渗工艺制备铝基复合材料的方法

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Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105761773A (zh) * 2016-03-07 2016-07-13 镇江纽科利核能新材料科技有限公司 乏燃料贮运用中子吸收材料的制备方法
CN105761773B (zh) * 2016-03-07 2017-09-29 镇江纽科利核能新材料科技有限公司 乏燃料贮运用中子吸收材料的制备方法
CN107353008A (zh) * 2017-06-20 2017-11-17 西安交通大学 一种层状金属‑陶瓷复合材料零件的制备方法
CN110983092A (zh) * 2019-12-12 2020-04-10 中国科学院长春光学精密机械与物理研究所 一种无压浸渗炉和制备颗粒增强铝基复合材料的方法
CN117026029A (zh) * 2023-08-09 2023-11-10 仲恺农业工程学院 一种高强高阻尼铝锌双金属合金及其制备方法
CN117026029B (zh) * 2023-08-09 2024-03-01 仲恺农业工程学院 一种高强高阻尼铝锌双金属合金及其制备方法
US12416068B2 (en) 2023-08-09 2025-09-16 Zhongkai University Of Agriculture And Engineering High-strength and high-damping aluminum-zinc bimetal alloy and preparation method thereof
CN117444180A (zh) * 2023-10-31 2024-01-26 北方工业大学 一种残余铝料易分离的无压浸渗工艺制备铝基复合材料的方法
WO2025091802A1 (fr) * 2023-10-31 2025-05-08 北方工业大学 Procédé de préparation d'un matériau composite à base d'aluminium par un processus d'infiltration sans pression capable de séparer facilement un matériau d'aluminium résiduel

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