Preparation and Mechanical Properties of Si-C-O Long Fiber/Alumina Matrix Composite

Kamino, Yoshitaka; Hirata, Yoshihiro; Kokusho, Tetsuro; Hamaishi, Kazuto; Morita, Harumi; Tabata, Ichiro

doi:10.2109/jcersj.103.1033

Cited by 3 publications

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“…Vacuum sin tering of the SiCO bers/alumina matrix composites at 12001300 C provided a signicant nonlinear fracture behavior in the exural stressstrain curves based on the berpullout from the matrix. 13) However, sintering of the composite in air produced the intermediate layer of the SiO 2 Al 2 O 3 system between the alumina matrix and SiCO bers due to the oxidation of the bers. The formation of the SiO 2 Al 2 O 3 layer reduced the exural strength of the com posite, which showed a brittle fracture behavior.…”

Section: Introductionmentioning

confidence: 99%

Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/Mullite Matrix Composites

Dong

Hirata

2003

J. Ceram. Soc. Japan

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Oxidation resistance of SiC satin fabric (2529 vol÷) or aluminosilicate plain fabric (2533 vol÷)/mullite matrix porous composites was investigated at 10001200 C in air for 24 h using thermogravimetric analysis. The composites were produced by a polymer impregnation and pyrolysis (PIP) method using a mullite precursor solution of the mixtures of Si(OC 2 H 5 ) 4 and Al(NO 3 ) 3 . The oxidation rate of the sintered SiC bers with a stoichiometric SiC composition and wellcrystallized microstructure was controlled by the diusion process of gases through dense SiO 2 layer formed on the SiC surface. The activation energy for the oxidation of the SiC bers was 299 kJ/mol. This value was close to the activation energy for the diusion of oxygen atom in silica glass. The SiC satin fabric/mullite matrix composite heated in an Ar atmosphere showed pseu doductility due to the delamination along the fabric layers. The four pointexural strength decreased slightly with increasing heat treatment temperature. However, the composite heated in air at 11001200 C showed brittle fracture behavior without delamination because of the increased strength of interfacial bond between the oxidized SiC bers and mullite matrix. On the other hand, the amorphous aluminosilicate bers/mullite matrix composite showed little weight change during the heat treatment at 10001200 C. Crystallization of mullite occurred in the mullite precursorderived amorphous solid and aluminosilicate bers at 1100 and 1200 C in air, respectively. However, no microstructural change was observed in the heat treated composite. The signicant pseudoductility and strength of the aluminosilicate plain fabric/mullite matrix composite were maintained after the heat treatment. The fracture energy increased with increasing heat treatment temperature.

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Section: Introductionmentioning

confidence: 99%

Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/Mullite Matrix Composites

Dong

Hirata

2003

J. Ceram. Soc. Japan

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Effect of sintering additives on mechanical properties of Cf/SiC composites

2002

Materials Chemistry and Physics

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Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/ Mullite Matrix Composites (Part 2)

Dong

HIRATA

2005

J. Ceram. Soc. Japan

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Influence of heat treatment at 10001500 C for 24 h on phases, microstructures and mechanical properties was studied for laminated SiC satin or aluminosilicate plain fabric/mullite matrix composites. Composites were produced by a polymer impregnation and pyrolysis method (PIP) using a mullite precursor. A mullite precursor solution of the mixtures of Si(OC 2 H 5 ) 4 and Al(NO 3 ) 3 was impregnated into the green layered fabric/mullite powder (filler) composite and was pyrolyzed at 500 C in air. This polymer impregnation and pyrolysis process was repeated 10 times. The SiC fabric (2527 vol÷)/mullite matrix composite with a relative density 7275÷ showed weight loss after heat treatment in an Ar atmosphere (oxygen partial pressure`0.75 Pa) at 1300 1500 C. This weight loss was due to the formation of volatile SiO gas resulting from the pyrolysis of mullite matrix (3Al 2 O 3 E2SiO 2 (s)¨3Al 2 O 3 (s){2SiO(g){O 2 (g)) and active oxidation of the SiC fiber (SiC(s){O 2 (g) SiO(g){CO(g)). The heattreated SiC fabric/mullite matrix composites showed an elastic deformation in the initial stage of the stressdisplacement curve, followed by pseudoductility. The strength (186 MPa) after the 1000 C heat treatment decreased to 17 MPa after the 1500 C heat treatment. The energy of fracture was 14 kJ/ m 2 in the heat treatment temperature range from 1000 to 1500 C.On the other hand, the aluminosilicate fabric (2530 vol÷)/mullite matrix composite with a relative density 7173÷ showed no weight loss after heat treat ment at 10001500 C in air. The porosity of the composite decreased with increasing heat treatment temperature because of the densification of the mullite matrix. This composite also showed pseudoductility after the heat treatment. The strength for the composite was slightly enhanced by increasing the heat treatment temperature.

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Preparation and Mechanical Properties of Si-C-O Long Fiber/Alumina Matrix Composite

Cited by 3 publications

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Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/Mullite Matrix Composites

Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/Mullite Matrix Composites

Effect of sintering additives on mechanical properties of Cf/SiC composites

Influence of Heat Treatment on Phases, Microstructures and Mechanical Properties of Laminated Fabric (SiC and Aluminosilicate)/ Mullite Matrix Composites (Part 2)

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