A numerical study on the thermal expansion coefficients of fiber
A numerical study on the thermal expansion coefficients of fiber A numerical study on the thermal expansion coefficients of fiber
39 expect the coefficient of thermal expansion of a composite to follow simple law of mixtures given by: α = α υ + α υ (3.6) c f f m m where α c , α f , α m are thermal expansion coefficients of the composite, filler and matrix respectively and υ f and υ m are the volumetric fractions of the filler and the matrix. Because of the differences in the thermal expansivities of the phases a state of micro-stress often exists between them. These stresses influence the thermal expansion behavior of the body. Thus, its thermal expansion coefficient does not follow the rule of mixtures. 3.4.1.2 Equation of Thomas as Thomas (Sideridis, 1994) put forward an empirical solution which can be written α = α υ + α υ (3.7) a c a f f a m m where a may vary from -1 to +1, and γ is the volumetric thermal expansion coefficient which is defined as α c = 3α for an isotropic composite. However, for a unidirectional composite, which is isotropic in the two transverse directions, the relation between volumetric thermal expansion coefficient and longitudinal and transverse thermal expansion coefficients can be written as α = α + 2α (3.8) c 1 2 where α 1 is the thermal expansion coefficient in the longitudinal direction and α 2 is the thermal expansion coefficient in the transverse direction. The empirical nature of the equation makes it suitable for most filed systems by the correct use of the adjustable constant.
40 3.4.1.3 Equation of Van Fo Fy In a series of articles by Van Fo Fy (1965), thermal expansion coefficients for matrices reinforced by continuous fibers are developed by means of a detailed stress analysis. As a result of this work, the thermal expansion coefficient in the longitudinal direction (α 1 ) is α 1 m ( ) ( 1+ ν ) ( )( ) m E f υf − 1+ ν f12 E1 − E mυm α m − αf ( ν m − ν f12 ) E 1 = α − (3.9) and the thermal expansion coefficient in the transverse direction (α 2 ) is α 2 ( α − α ) ν − ( α − α )( 1+ ν ) − ν m 12 = α m + m 1 12 m f f12 (3.10) ν m − ν f12 ν where E f , E m are elastic moduli and ν f , ν m are the Poisson’s ratios of fiber and matrix respectively. E 1 is the elastic modulus for the longitudinal direction of composite and ν 12 is the Poisson’s ratio of the composite. However, the values predicted by these expressions are very sensitive to variations in E 1 and deviations arose by the experimental error may cause considerable discrepancies. E 1 can be found, using the simple rule of mixtures, as E = + (3.11) 1 E f υf E mυ m 3.4.1.4 Equation of Cribb Cribb (Sideridis, 1994) adopted an approach in which no limitations are made on the shape or size of the fillers. The phases are assumed to be homogeneous, isotropic and linearly elastic. The equation is given as α = θ α + θ α (3.12) c 1 m 2 f
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39<br />
expect <strong>the</strong> coefficient <strong>of</strong> <strong>the</strong>rmal expansi<strong>on</strong> <strong>of</strong> a composite to follow simple law <strong>of</strong><br />
mixtures given by:<br />
α = α υ + α υ<br />
(3.6)<br />
c<br />
f<br />
f<br />
m<br />
m<br />
where α c , α f , α m are <strong>the</strong>rmal expansi<strong>on</strong> <strong>coefficients</strong> <strong>of</strong> <strong>the</strong> composite, filler and matrix<br />
respectively and υ f and υ m are <strong>the</strong> volumetric fracti<strong>on</strong>s <strong>of</strong> <strong>the</strong> filler and <strong>the</strong> matrix.<br />
Because <strong>of</strong> <strong>the</strong> differences in <strong>the</strong> <strong>the</strong>rmal expansivities <strong>of</strong> <strong>the</strong> phases a state <strong>of</strong><br />
micro-stress <strong>of</strong>ten exists between <strong>the</strong>m. These stresses influence <strong>the</strong> <strong>the</strong>rmal<br />
expansi<strong>on</strong> behavior <strong>of</strong> <strong>the</strong> body. Thus, its <strong>the</strong>rmal expansi<strong>on</strong> coefficient does not<br />
follow <strong>the</strong> rule <strong>of</strong> mixtures.<br />
3.4.1.2 Equati<strong>on</strong> <strong>of</strong> Thomas<br />
as<br />
Thomas (Sideridis, 1994) put forward an empirical soluti<strong>on</strong> which can be written<br />
α = α υ + α υ<br />
(3.7)<br />
a<br />
c<br />
a<br />
f<br />
f<br />
a<br />
m<br />
m<br />
where a may vary from -1 to +1, and γ is <strong>the</strong> volumetric <strong>the</strong>rmal expansi<strong>on</strong><br />
coefficient which is defined as α c = 3α for an isotropic composite. However, for a<br />
unidirecti<strong>on</strong>al composite, which is isotropic in <strong>the</strong> two transverse directi<strong>on</strong>s, <strong>the</strong><br />
relati<strong>on</strong> between volumetric <strong>the</strong>rmal expansi<strong>on</strong> coefficient and l<strong>on</strong>gitudinal and<br />
transverse <strong>the</strong>rmal expansi<strong>on</strong> <strong>coefficients</strong> can be written as<br />
α = α + 2α<br />
(3.8)<br />
c<br />
1<br />
2<br />
where α 1 is <strong>the</strong> <strong>the</strong>rmal expansi<strong>on</strong> coefficient in <strong>the</strong> l<strong>on</strong>gitudinal directi<strong>on</strong> and α 2 is<br />
<strong>the</strong> <strong>the</strong>rmal expansi<strong>on</strong> coefficient in <strong>the</strong> transverse directi<strong>on</strong>. The empirical nature <strong>of</strong><br />
<strong>the</strong> equati<strong>on</strong> makes it suitable for most filed systems by <strong>the</strong> correct use <strong>of</strong> <strong>the</strong><br />
adjustable c<strong>on</strong>stant.