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Developments in Ceramic Materials Research

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178<br />

M. A. Sheik<br />

Dur<strong>in</strong>g the cool<strong>in</strong>g from a typically high process<strong>in</strong>g temperature of CMCs, very high<br />

thermal stresses ensue as a result of the thermal mismatch between the re<strong>in</strong>forcement and the<br />

matrix. In the <strong>in</strong>stance of a fibrous composite, an <strong>in</strong>terfacial pressure develops dur<strong>in</strong>g the<br />

cool<strong>in</strong>g phase. Thermal stresses generated are dependent on the re<strong>in</strong>forcement volume<br />

fraction ‘V’, re<strong>in</strong>forcement geometry, thermal mismatch (αF < αM) temperature <strong>in</strong>terval ‘ΔT’<br />

and also the modulus ratio (EF/EM).<br />

Generally, dur<strong>in</strong>g cool<strong>in</strong>g, the matrix tends to contract more than the re<strong>in</strong>forcement<br />

putt<strong>in</strong>g the re<strong>in</strong>forcement <strong>in</strong> compression (αF < αM). This mismatch is difficult to elim<strong>in</strong>ate,<br />

but it can be manipulated to extract desirable characteristics of the composite. Through a<br />

prudent choice of components, it is feasible to acquire a favourable residual stress pattern<br />

rather than adverse f<strong>in</strong>al attributes at the end of the process<strong>in</strong>g. In CMCs, crack deflection at<br />

the fibre/matrix <strong>in</strong>terface is beneficial for the augmentation of toughness <strong>in</strong> the composite.<br />

Frequently, <strong>in</strong>terfacial coat<strong>in</strong>gs, that are primarily mechanical <strong>in</strong> nature, are <strong>in</strong>troduced <strong>in</strong><br />

CMCs to optimise stress distribution and bond<strong>in</strong>g at the fibre/matrix <strong>in</strong>terface.<br />

The longitud<strong>in</strong>al expansion coefficient of a composite is given by:<br />

where:<br />

Similarly, the transverse expansion coefficient of a composite is expressed by:<br />

and ‘V ’ is the volume fraction, ‘E ’ is the Young’s Modulus, ‘ν ’ is the Poisson’s ratio and<br />

the subscripts ‘C ’, ‘F ’ and ‘M ’ refer to composite, fibre and matrix, respectively [13].<br />

For a unidirectional fibre re<strong>in</strong>forced composite, a prediction of thermal conductivity <strong>in</strong><br />

the longitud<strong>in</strong>al (l) and the transverse (t) directions is proposed by Behrens [14] as:<br />

k 1 = kcl<br />

= k FlVF<br />

+ k MV<br />

k2<br />

= kct<br />

=<br />

k<br />

kFtk<br />

M<br />

V + k V<br />

Ft<br />

f<br />

M<br />

M<br />

M<br />

where, subscripts ‘1’ and ‘2’ denote the pr<strong>in</strong>cipal directions of the unidirectional composite.<br />

In case of woven fabric-re<strong>in</strong>forced composites, such formulation is not applicable s<strong>in</strong>ce nonhomogenous<br />

material phases are <strong>in</strong>termixed and <strong>in</strong>tertw<strong>in</strong>ed <strong>in</strong> one volume. One direct<br />

(2)<br />

(3)<br />

(4)<br />

(5)<br />

(6)

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