R Venkatesh/ Ceramics International 28(2002)565-573 to fiber roughness was about 20 times larger than the clamping due to fiber roughness at the fiber/ SnO, inter- tensile thermal radial strain, AaAT. In Saphikon /SnO2/ face in ASG composites glass matrix composites, the roughness induced com The bending strength of AG and ASG matrix com pressive strain was only three times larger than the ten- posites as a function of volume fraction of fibers is sile thermal strain. This indicates the strong mechanical shown in Table 7. volume fraction of S and SSg 50um Energy Fig 8.(a) Fracture surface of saphikon/SnO/glass composites;(b) EDS analysis in region marked(A)showing only Al and no Sn.to fiber roughness was about 20 times larger than the tensile thermal radial strain, T. In Saphikon/SnO2/ glass matrix composites, the roughness induced compressive strain was only three times larger than the tensile thermal strain. This indicates the strong mechanical clamping due to fiber roughness at the fiber/SnO2 interface in ASG composites. The bending strength of AG and ASG matrix composites as a function of volume fraction of fibers is shown in Table 7. Volume fraction of SG and SSG Fig. 8. (a) Fracture surface of saphikon/SnO2/glass composites; (b) EDS analysis in region marked (A) showing only Al and no Sn. R. Venkatesh / Ceramics International 28 (2002) 565–573 571