Abstract
In this work, chemical vapor infiltration (CVI) was combined with reactive melt infiltration (RMI) using Ti–6Al–4V titanium alloy powder to prepare Cf/C–TiC composites. The microstructure and composition of Cf/C–TiC composites were characterized by scanning electron microscopy (SEM) and X-ray diffraction (XRD). The flexural properties of the composites were also analyzed. The results indicated that the Ti–6Al–4V titanium alloy infiltrated the Cf/C preform and reacted with the pyrolytic carbon (PyC) to form a TiC–VC and Al4C3 matrix, and no residual Ti, Al, or V was detected. Moreover, Al4C3 was concentrated and independently distributed, whereas Ti and V reacted with C to form a TiC–VC solid solution. The porosity was 6.75%, and the bulk density of Cf/C–TiC was 1.96 g/cm3. The flexural strength, flexural modulus, and failure strains were 256 ± 18 MPa, 89 ± 9 GPa, and 0.93 ± 0.13%, respectively. The work of fracture of the Cf/C–TiC composite was about 6.8 ± 0.38 KJ/m2. Due to the propagation and deflection of cracks, as well as debonding and fiber pullout, the Cf/C–TiC composite showed ductile fracture behavior.
Highlights
Continuous fiber-reinforced ceramic matrix composites (CMCs) have been widely used in aerospace and nuclear industries due to their high-temperature oxidation resistance and good toughness
An unreacted pyrolytic carbon (PyC) layer exists between the ceramic matrix and carbon fibers, which acts as a good interface between the ceramic phase and fibers when the Cf /C–TiC is under load
The porosity and density of the Cf /C preform before infiltration were 22.83% and 1.30 g/cm3, respectively, whereas the porosity and density of the composites after reactive melt infiltration (RMI) were 6.75% and 1.96 g/cm3, respectively. This shows that the Ti–6Al–4V titanium alloy powder infiltrated the Cf /C preform, which reduced the porosity and increased the density of the material
Summary
Continuous fiber-reinforced ceramic matrix composites (CMCs) have been widely used in aerospace and nuclear industries due to their high-temperature oxidation resistance and good toughness. Carbon fiber-reinforced CMC preparation methods include chemical vapor deposition (CVD) [1], polymer impregnation and pyrolysis (PIP) [2,3], and reactive melt infiltration (RMI) [4]. CVD and PIP methods increase the cost of fabrication processes due to preparation times of hundreds of hours. The RMI method has been widely studied due to its short preparation time, low cost, and near-net-shape production [5]. An unreacted pyrolytic carbon (PyC) layer exists between the ceramic matrix and carbon fibers, which acts as a good interface between the ceramic phase and fibers when the Cf /C–TiC is under load. Due to the load transmission and crack deflection at the interface, composites formed by RMI tend to have higher mechanical properties [6,7,8]
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