NO169646B - PROCEDURE FOR MANUFACTURING ARTICLES OF COMPOSITION MATERIALS - Google Patents

PROCEDURE FOR MANUFACTURING ARTICLES OF COMPOSITION MATERIALS Download PDF

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Publication number
NO169646B
NO169646B NO900726A NO900726A NO169646B NO 169646 B NO169646 B NO 169646B NO 900726 A NO900726 A NO 900726A NO 900726 A NO900726 A NO 900726A NO 169646 B NO169646 B NO 169646B
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aluminum
silicon nitride
nitride
metal
procedure
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NO900726A
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Norwegian (no)
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NO900726D0 (en
NO169646C (en
NO900726L (en
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Arne Seltveit
Constantinos Diavatis
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Sinvent As
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Priority to NO900726A priority Critical patent/NO169646C/en
Publication of NO900726D0 publication Critical patent/NO900726D0/en
Priority to AU72380/91A priority patent/AU7238091A/en
Priority to PCT/NO1991/000020 priority patent/WO1991012350A1/en
Publication of NO900726L publication Critical patent/NO900726L/en
Publication of NO169646B publication Critical patent/NO169646B/en
Publication of NO169646C publication Critical patent/NO169646C/en

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    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/009—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone characterised by the material treated
    • 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
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
    • C04B35/581—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on aluminium nitride
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/64—Burning or sintering processes
    • C04B35/65—Reaction sintering of free metal- or free silicon-containing compositions
    • C04B35/652—Directional oxidation or solidification, e.g. Lanxide process
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/45—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements
    • C04B41/50—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials
    • C04B41/5053—Coating or impregnating, e.g. injection in masonry, partial coating of green or fired ceramics, organic coating compositions for adhering together two concrete elements with inorganic materials non-oxide ceramics
    • C04B41/5062—Borides, Nitrides or Silicides
    • C04B41/5063—Aluminium nitride
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B41/00—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone
    • C04B41/80—After-treatment of mortars, concrete, artificial stone or ceramics; Treatment of natural stone of only ceramics
    • C04B41/81—Coating or impregnation
    • C04B41/85—Coating or impregnation with inorganic materials
    • C04B41/87—Ceramics
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Ceramic Engineering (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Structural Engineering (AREA)
  • Inorganic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Materials Applied To Surfaces To Minimize Adherence Of Mist Or Water (AREA)
  • Confectionery (AREA)
  • Insulated Conductors (AREA)
  • Ceramic Products (AREA)

Description

Den foreliggende oppfinnelse vedrører en ny fremgangsmåte for fremstilling av komposittmaterialer som omfatter aluminiumnitrid og aluminiummetall. Komposittmaterialer av keramiske partikler eller fibre med metallisk matriks har i flere tiår vært benyttet for ulike formål. Materialene fremstilles gjerne ad pulvermetallurgisk vei ved at man fremstiller en pulver-blanding av de aktuelle komponentene, former de aktuelle gjenstandene med kjente formgivningsmetoder og derefter sintrer gjenstandene ved optimale temperaturer i en ovnsatmosfære med ønsket gass-sammensetning og totaltrykk. Alternativt kan man blande inn de keramiske partiklene i flytende metall og derefter formgi materialet ved f.eks. støping. The present invention relates to a new method for the production of composite materials comprising aluminum nitride and aluminum metal. Composite materials of ceramic particles or fibers with a metallic matrix have been used for several decades for various purposes. The materials are usually produced by powder metallurgy by preparing a powder mixture of the relevant components, forming the relevant objects using known shaping methods and then sintering the objects at optimum temperatures in a furnace atmosphere with the desired gas composition and total pressure. Alternatively, one can mix the ceramic particles into liquid metal and then shape the material by e.g. casting.

En tredje metode - som spesielt anvendes for fiberholdige kompositter - er infiltrering av flytende metall i en fibermasse som er pakket til ønsket tetthet i en beholder (preform). A third method - which is particularly used for fiber-containing composites - is the infiltration of liquid metal into a fiber mass that is packed to the desired density in a container (preform).

Komposittmaterialer av aluminiumnitrid og aluminiummetall er tidigere beskrevet i US patentskrift 3.328.280 (1967) og 3.408.312 (1968), begge tilhørende N. E. Richards, J.S. Berry og T. J. Johnston (Reynold Metals). I disse angis at slike materialer kan fremstilles ved kjente metoder - som angitt ovenfor - ut fra blandinger av aluminiumnitrid-pulver og aluminiummetall-pulver. En foretrukket metode ifølge de nevnte patenter er varmpressing av pulverblandingen i grafittformer og sintring under trykk på 1600 psi (~ 11 MPa) ved temperatur ca. 1750°C ± 50°C. Materialene angis å ha relativt høy elektrisk ledningsevne og god bestandighet overfor flytende aluminium og alkalifluoridsmelter. Composite materials of aluminum nitride and aluminum metal were previously described in US Patents 3,328,280 (1967) and 3,408,312 (1968), both to N.E. Richards, J.S. Berry and T.J. Johnston (Reynold Metals). These state that such materials can be produced by known methods - as stated above - from mixtures of aluminum nitride powder and aluminum metal powder. A preferred method according to the aforementioned patents is hot pressing of the powder mixture in graphite molds and sintering under pressure of 1600 psi (~ 11 MPa) at a temperature of approx. 1750°C ± 50°C. The materials are stated to have relatively high electrical conductivity and good resistance to liquid aluminum and alkali fluoride melts.

I henhold til oppfinnelsen tilveiebringes en fremgangsmåte for fremstilling av gjenstander av komposittmaterialer som omfatter aluminiumnitrid og aluminiummetall. Fremgangsmåten karakteriseres ved at en porøs silisiumnitrid-gjenstand infiltreres med flytende aluminium eller aluminiumlegering, og omsetning mellom silisiumnitrid og inntrengt aluminium frembringes ved en temperatur over smeltepunktet for aluminium. According to the invention, a method is provided for the production of objects from composite materials comprising aluminum nitride and aluminum metal. The method is characterized by the fact that a porous silicon nitride object is infiltrated with liquid aluminum or aluminum alloy, and reaction between silicon nitride and penetrated aluminum is produced at a temperature above the melting point of aluminum.

Foreliggende oppfinnelse er således basert på konvertering in situ av silisiumnitrid til aluminiumnitrid ved tilsats av flytende aluminium, slik som kan illustreres ved reaksjons-ligningen The present invention is thus based on the in situ conversion of silicon nitride to aluminum nitride by the addition of liquid aluminium, as can be illustrated by the reaction equation

Termodynamiske data for henholdsvis silisiumnitrid og aluminiumnitrid viser at ved temperaturer over smeltepunktet for rent aluminium (660°C) er likevekten sterkt forskjøvet mot høyre. Laboratorieforsøk har vist at ved å velge et egnet silisiumnitrid-materiale lar det seg gjøre å infiltrere dette fullstendig med flytende aluminium ved å holde silisiumnitridmaterialet nedsenket i flytende aluminiummetall i en viss tid. Silisiumnitridet omsettes med infiltrert metall som angitt ovenfor, slik at det dannes et kompositt-materiale som hoved-sakelig består av aluminiumnitrid og en silisiumholdig aluminiumlegering. Legeringens silisiuminnhold vil være avhengig av bl.a. eksponeringstid, temperatur og metallpermeabiliteten av den opprinnelige silisiumnitrid-gjenstanden. Thermodynamic data for silicon nitride and aluminum nitride respectively show that at temperatures above the melting point of pure aluminum (660°C) the equilibrium is strongly shifted to the right. Laboratory tests have shown that by choosing a suitable silicon nitride material it is possible to infiltrate it completely with liquid aluminum by keeping the silicon nitride material immersed in liquid aluminum metal for a certain time. The silicon nitride is reacted with infiltrated metal as indicated above, so that a composite material is formed which mainly consists of aluminum nitride and a silicon-containing aluminum alloy. The alloy's silicon content will depend on i.a. exposure time, temperature and the metal permeability of the original silicon nitride object.

Silisiumnitrid-utgangsmaterialet kan fremstilles på flere måter, men det foretrekkes å la silisiummetall reagere med nitrogen ved forhøyet temperatur som i og for seg kjent. Silisiumpulveret kan hensiktsmessig gis en form nær den ønskede sluttform, hvorefter sammensintring og nitrering finner sted. Det er ikke nødvendig at alt silisium blir nitrert, idet eventuelle rester av Si i silisiumnitridet ikke har noen uheldig virkning. I enkelte tilfeller synes det til og med som om det kan være gunstig for den påfølgende konvertering. The silicon nitride starting material can be prepared in several ways, but it is preferred to allow silicon metal to react with nitrogen at an elevated temperature as is known per se. The silicon powder can conveniently be given a shape close to the desired final shape, after which sintering and nitriding take place. It is not necessary for all silicon to be nitrided, as any residual Si in the silicon nitride has no adverse effect. In some cases, it even seems that it can be beneficial for the subsequent conversion.

Det settes her ikke spesielt store krav til tetthet og mekanisk styrke av silisiumnitridmaterialet, som derfor kan fremstilles med relativt lave omkostninger. Konverteringen er også en enkel prosess, og følgelig vil det ved bruk av den her beskrevne fremgangsmåte være mulig å produsere de aktuelle kompositter med relativt lave kostnader. There are no particularly high requirements for the density and mechanical strength of the silicon nitride material, which can therefore be produced at relatively low costs. The conversion is also a simple process, and consequently, by using the method described here, it will be possible to produce the composites in question at relatively low costs.

Et sterkt fordyrende ledd i produksjonen er ofte efter-bearbeiding av ferdig sintrede keramer eller keram/metall-komposittet. Dette skyldes at de fleste slike materialer er meget hårde og vanskelig lar seg bearbeide med tradisjonelt slipe- og maskineringsutstyr. Ved fremstilling av reaksjons-bundne silisiumnitrid-gjenstander kan bearbeidingsproblemene forenkles vesentlig hvis sintringen foretas i to trinn. Først foretas en delvis sintring og nitrering ved 1100-1200°C, derefter foretas nødvendig maskinell bearbeiding og så foretas sluttnitreringen ved ca. 1400°C. Nitreringen medfører bare ubetydelige endringer i ytre dimensjoner. A highly expensive part of production is often post-processing of finished sintered ceramics or the ceramic/metal composite. This is because most such materials are very hard and difficult to process with traditional grinding and machining equipment. When producing reaction-bonded silicon nitride objects, the processing problems can be simplified significantly if the sintering is carried out in two stages. First, a partial sintering and nitriding is carried out at 1100-1200°C, then the necessary mechanical processing is carried out and then the final nitriding is carried out at approx. 1400°C. The nitriding causes only insignificant changes in external dimensions.

Laboratorieforsøk har vist at også den ovenfor beskrevne konvertering av silisiumnitrid til aluminiumnitrid bare ledsages av meget små endringer i ytre dimensjoner. Ved å foreta en kostnadsmessig sett rimelig bearbeiding av den delvis nitrerte silisiumnitrid-gjenstand kan bearbeidingskostnadene for den ferdige aluminiumnitrid/aluminiummetall-kompositt reduseres til et minimum. Laboratory tests have shown that the above-described conversion of silicon nitride to aluminum nitride is also only accompanied by very small changes in external dimensions. By carrying out a cost-effective processing of the partially nitrided silicon nitride object, the processing costs for the finished aluminum nitride/aluminium metal composite can be reduced to a minimum.

En annen fordel som oppnås ved hjelp av den beskrevne fremstillingsmåte er at det i det ferdige produkt foreligger sterke direkte-bindinger mellom de enkelte aluminiumnitrid-partiklene slik at den mekaniske fasthet ikke endres drastisk ved temperaturer over metallfasens smeltepunkt. Disse bindingene er etablert ved nitreringen av silisium under fremstillingen av silisiumnitrid-gjenstanden, og bindingene synes å opprettholdes under konverteringen til aluminiumnitrid. Another advantage achieved by the described manufacturing method is that in the finished product there are strong direct bonds between the individual aluminum nitride particles so that the mechanical strength does not change drastically at temperatures above the melting point of the metal phase. These bonds are established by the nitriding of silicon during the manufacture of the silicon nitride article, and the bonds appear to be maintained during the conversion to aluminum nitride.

Den elektriske ledningsevne av materialet er sterkt avhengig av bl.a. mengdeforholdet mellom nitrid- og metallfase. Ved bruk av foreliggende oppfinnelse kan således den elektriske ledningsevne varieres innen vide grenser ved f.eks. å velge silisiumnitridmaterialer med forskjellig porøsitet og pore-fordeling. Hvis det aktuelle komposittmateriale primært skal tjene som et strømførende materiale, vil det være riktig å benytte et relativt porøst silisiumnitridmateriale. Skal derimot materialet i første rekke tjene som konstruksjons-materiale er det logisk å foreta konvertering av et tettere og sterkere silisiumnitrid-materiale. The electrical conductivity of the material is strongly dependent on i.a. the quantity ratio between nitride and metal phase. When using the present invention, the electrical conductivity can thus be varied within wide limits by e.g. to choose silicon nitride materials with different porosity and pore distribution. If the composite material in question is primarily to serve as a current-carrying material, it would be correct to use a relatively porous silicon nitride material. If, on the other hand, the material is primarily to serve as a construction material, it is logical to convert a denser and stronger silicon nitride material.

Istedenfor å foreta infiltrasjonen av silisiumnitrid-utgangsmaterialet med aluminium, kan den også foretas med en aluminiumlegering, og en rekke legeringselementer er her mulige, f.eks. magnesium, kobber, sink etc. Man vil da kunne oppnå en bedre inntrengning i silisiumnitrid-utgangsmaterialet, og vil også kunne få tilført visse ønskede egenskaper så som øket ledningsevne. Instead of carrying out the infiltration of the silicon nitride starting material with aluminium, it can also be carried out with an aluminum alloy, and a number of alloying elements are possible here, e.g. magnesium, copper, zinc etc. You will then be able to achieve a better penetration into the silicon nitride starting material, and will also be able to add certain desired properties such as increased conductivity.

Eksempel 1 Example 1

Et prøvestykke av sintret silisiumnitrid (RBSN) med dimensjoner ca. 10 x 9 x 24 mm ble plassert i en grafittdigel sammen med ca. 40 g aluminiummetall og oppvarmet til 900°C i en laboratorieovn med ovnsatmosfære bestående av argon. Digelen med innhold ble holdt ved 900°C i 7 døgn. Prøven ble så tatt ut av digelen med aluminiumsmelte, og mineralsammensetningen ble analysert kvalitativt ved røntgendiffraksjon. Fig. la og lb viser røntgendiffraktogrammer for prøven hhv. før og efter eksponering. Som det fremgår av diagrammene er det foregått en praktisk talt fullstendig konvertering av silisiumnitrid til aluminiumnitrid. A sample of sintered silicon nitride (RBSN) with dimensions approx. 10 x 9 x 24 mm was placed in a graphite crucible together with approx. 40 g of aluminum metal and heated to 900°C in a laboratory furnace with a furnace atmosphere consisting of argon. The crucible with contents was kept at 900°C for 7 days. The sample was then taken out of the crucible with molten aluminium, and the mineral composition was analyzed qualitatively by X-ray diffraction. Fig. la and lb show X-ray diffractograms for the sample, respectively. before and after exposure. As can be seen from the diagrams, a practically complete conversion of silicon nitride to aluminum nitride has taken place.

Volumvekt av prøvestykket før og efter konvertering var henholdsvis 2,32 g/cm<3> og 3,09 g/cm<3>. Totalporøsiteten av silisiumnitridprøven var ca. 25%, åpen porøsitet var 17%. Åpen porøsitet av konvertert materiale var 1-2%. Volumetric weight of the sample before and after conversion was 2.32 g/cm<3> and 3.09 g/cm<3> respectively. The total porosity of the silicon nitride sample was approx. 25%, open porosity was 17%. Open porosity of converted material was 1-2%.

Eksempel 2 Example 2

Et prøvestykke av reaksjonssintret Si3N4 (RBSN) med dimensjoner 10 x 10 x 20 mm ble eksponert i 3 døgn i en smelte av aluminiumlegering 2004 (AA 7001) under forøvrig samme betingelser som angitt i eksempel 1. Røntgendiffraktogrammet av eksponert materiale viser at praktisk talt all Si3N4 er omsatt, kfr. fig. 2 A test piece of reaction sintered Si3N4 (RBSN) with dimensions 10 x 10 x 20 mm was exposed for 3 days in a melt of aluminum alloy 2004 (AA 7001) under otherwise the same conditions as stated in example 1. The X-ray diffractogram of exposed material shows that practically all Si3N4 is reacted, see fig. 2

Claims (4)

1. Fremgangsmåte for fremstilling av gjenstander av komposittmaterialer som omfatter aluminiumnitrid og aluminiummetall, karakterisert ved at en porøs silisiumnitrid-gjenstand infiltreres med flytende aluminium eller aluminiumlegering, og omsetning mellom silisiumnitrid og inntrengt aluminium frembringes ved en temperatur over smeltepunktet for aluminium.1. Method for producing objects from composite materials comprising aluminum nitride and aluminum metal, characterized in that a porous silicon nitride object is infiltrated with liquid aluminum or aluminum alloy, and conversion between silicon nitride and infiltrated aluminum is produced at a temperature above the melting point of aluminum. 2. Fremgangsmåte ifølge krav 1, karakterisert ved at det anvendes et sintret silisiumnitrid-utgangsmateriale med tilnærmet samme dimensjoner som den ønskede kompositt-gjenstand.2. Method according to claim 1, characterized in that a sintered silicon nitride starting material with approximately the same dimensions as the desired composite object is used. 3. Fremgangsmåte ifølge krav 1 eller 2, karakterisert ved at det anvendes et silisiumnitrid-utgangsmateriale som er sintret i to trinn med be-arbeidning mellom trinnene.3. Method according to claim 1 or 2, characterized in that a silicon nitride starting material is used which is sintered in two stages with processing between the stages. 4. Fremgangsmåte ifølge et av kravene 1 til 3, karakterisert ved at infiltreringen foretas med en aluminiumlegering.4. Method according to one of claims 1 to 3, characterized in that the infiltration is carried out with an aluminum alloy.
NO900726A 1990-02-15 1990-02-15 PROCEDURE FOR MANUFACTURING ARTICLES OF COMPOSITION MATERIALS NO169646C (en)

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Application Number Priority Date Filing Date Title
NO900726A NO169646C (en) 1990-02-15 1990-02-15 PROCEDURE FOR MANUFACTURING ARTICLES OF COMPOSITION MATERIALS
AU72380/91A AU7238091A (en) 1990-02-15 1991-02-13 Method for the preparation of articles of composite materials
PCT/NO1991/000020 WO1991012350A1 (en) 1990-02-15 1991-02-13 Method for the preparation of articles of composite materials

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Publication number Priority date Publication date Assignee Title
US5518061A (en) * 1988-11-10 1996-05-21 Lanxide Technology Company, Lp Method of modifying the properties of a metal matrix composite body
DE4118943A1 (en) * 1991-06-08 1992-12-10 Vaw Ver Aluminium Werke Ag METAL-CERAMIC COMPOSITE FROM A NITRIDIC MATRIX CONTAINING A THREE-DIMENSIONALLY CROSS-LINKED ALUMINUM-CONTAINING METAL PHASE
CA2138663A1 (en) * 1992-06-26 1994-01-06 Marc Stevens Newkirk A method of modifying the properties of a metal matrix composite body
US5848349A (en) * 1993-06-25 1998-12-08 Lanxide Technology Company, Lp Method of modifying the properties of a metal matrix composite body
DE4406191A1 (en) * 1994-02-25 1995-09-07 Ks Aluminium Technologie Ag Plain bearing

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US3408312A (en) * 1964-04-07 1968-10-29 Reynolds Metals Co Electrically conductive cermet compositions
US3328280A (en) * 1964-04-07 1967-06-27 Reynolds Metals Co Electrically conductive cermet compositions
JPS539254B2 (en) * 1973-03-26 1978-04-04
JPS5523892B2 (en) * 1973-04-03 1980-06-25
JPS5967336A (en) * 1982-10-07 1984-04-17 Toyota Motor Corp Manufacture of composite material
US4777014A (en) * 1986-03-07 1988-10-11 Lanxide Technology Company, Lp Process for preparing self-supporting bodies and products made thereby
US4828008A (en) * 1987-05-13 1989-05-09 Lanxide Technology Company, Lp Metal matrix composites

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NO900726D0 (en) 1990-02-15
NO169646C (en) 1992-07-22
WO1991012350A1 (en) 1991-08-22
AU7238091A (en) 1991-09-03
NO900726L (en) 1991-08-16

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