October 1996 through September 1997 - Oak Ridge National ...

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Fig. C.25. HREM image cfWO-Y2O3 interface showing an atomically abrupt transition between tbe two phases. Fig. C.26. Model of NiO-Y203 interface in which the phases share a common oxygen plane.
University of Massachusetts at Amherst, "High-Temperature Residual Stress Measurement of Sic- Fiber-Reinforced HMAS Class-Ceramic Matris Composite," K. fnkus and S. Wk@ju, HTML No. 97-039 RSUC When a fiber-reinforced ceramic matrix composite is creep-conditioned such that the applied load transfers from the matrix to the fibers and when the composite is cooled under load, a compressive residual stress is induced in the matrix as a result of a con5trained clastic rebound. This compressive residual stress increases the ultimate matrix cracking strcss of tlic composite (see H?'ML, Proposal No. 95- 043). X-ray diffraction residual strcss analysis results show that tlic residual stress in the matrix of NicalonTM/RMAS glass-ceramic matrix composite increased from -7 1 MPa (as-received specimen) to -1 24 MPa for a specimen creep-conditioned at 1 100°C for 12. h under a stress of 75 MPa, and to -1 90 MPa for a specimen treated at 1 1 00T for 30 h under a stress of 90 MPa. The residual stress nieasurement of the BMAS matrix was based on the peak shift ofthe (8 2 4) plane of barium osumilite phase. The compressive residual stress in the as-received specimen is because ofthe thermal expansion mismatch between the fibers and matrix upon cooling. The increase in the residual stress in the matrix of creepconditioned specimens is attributed to the effectiveness of creep-load transfer technique. l'he purpose of this studq was to better understand the behavior of residual stress induced in the NicalonlM/HMAS glass-ceramic matrii composite at high temperature. High temperature residual stress measurenicnts would provide data to characterizc the compressive residual stress in the matrix with respect to temperature. The H'I'XKD residual stress nicasurenients were done at temperatures of 300% and 550T, where the matrix does not creep. A problem arose at elevated temperature in that the barium osutnilite (8 2 4) reflection was no longer observable in the X-ray pattern because of the thermal motion of the atom reducing the scattered intensity. Further work is being considered for NSLS. Universitv of Massachusetts at Amherst, "Creep-Induced Residual Stress Strengthening im Fiber Reinforced Ceramic Matrix Composites," K. Jnkirs and S. lVi&iju, HTML No. 95-043 MCAUC/RSUC High temperature creep-conditioning of continuous fiber-reinforced ceramic matrix composites, in mhich the fiber? are more crcep-resistant than the matrix, causes the matrix to transfer its load to the fibers. Upon removal of the load after cooling to rooni temperature, a compressive residual stress is induced in the matrix by the elastic recovery ofthe iibers. This compressive residual stress in the matrix causes an increase in the matrix cracking stress ofthe composite, improving the reliability of the materials. The objective of this research was to study the effkctiveness of high teniperature creep conditioning in improving the matrix cracking stress. Laminated 0"/9O0NicalonTk1 fiber-reinforced HMAS glass-ceramic matrix composite specimens were creep-conditioned in tension at 1 100°C under constant stress. cooled uiidcr load to rooni temperature, and then unloaded. 'Thc applied crcep strcss ranged from 35 MPa to 90 Mf'a, and the creep times varied from 12 h to 100 h. The resulting room temperature tensile stress-strain behavior was determined, and acoustic emission activity was monitored during the tensile test to detect cracking activity. The residual stresses in the matrix of the as-received and creep-conditioned specimens were independently measured with X-ray diffraction. Creep-load transfer results showed that the increase in the proportional limit (Le., the onbet of significant matrix cracking) of the creep-conditioned speciinens mas attributed to the effectiveness of the creep-load transfer treatment in inducing a compressive residual stress in the matrix. Figure C.27 illustrates the tensile stress-strain behaviors of the as-received and crept specimens, showing a significant increase in the proportional limit ofthe specimen creep-conditioiicd under 75 MPa for 12 h. The acoustic cmission and X-ray diffraction data confirmed that the increase in thc observed proportional limit of the c-47
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OAK RIDGE NATIONAL LAB0 RAT0 RY 3 4
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High Temperature Materials Lahorato
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Hardness and elastic modulus proper
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AI'PENDJX A. STANDARD NONYROPKIETAR
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October 1996 through September 1997 - Oak Ridge National ...

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