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The experimental data can be linearly fitted in log-log diagrams in good agreement with the Paris law da = C (AK)m dN where C and m are material dependent constants. 0 ln(dK) Fig. 1. FCP curves for the neat epoxy 1 (O) and PDMS modified networks with 4% vol. (A), 8 % vol. ( ) and 15 % vol. , 1999, with kind permission from Kluwer Academic Publisher). 1 9 9 21 oo 000 o~e ~176 ~' ? ml/2) I 1 Fig. 2. 5 % vol. CTBN8. ). Some similar results on epoxy toughened networks have already been obtained [5,6,8,9,10].

Karger-Kocsis, J. (2000). In: Structure Development During Polymer Processing, pp. M and Fakirov, S. T. and Runt, J. (1989)J. Mater. , 24, 2637. Brown, N. M. (1983)J. Mater. , 18, 1405. Beerbaum, H. and Grellmann, W. (2000). In: Fracture of Polymers, Composites and Adhesives, ESIS Publ. 27, pp. G. and Pavan, A. , Grellmann, W. and Seidler, S. (2001). In: Deformation and Fracture Behavior of Polymers, pp. 161-180, Grellmann, W. and Seidler, S. J. and Delatycki, O. (1995)J. Mater. , 30, 3307 This Page Intentionally Left Blank The Application of Fracture Mechanics to Polymers.

Notes" data taken from Refs. [5,11]; for designations cf. Fig. I. g. skin-core morphology) may blur the use of fracture mechanics. The effect of morphology (spherulitic structure) on the fracture toughness proved to be also not negligible. Studies performed on J3-phase PP exhibited a strong dependence of the work of fracture parameters as a function on both crystallinity and mean MW [1,12]. In the literature highly contradictory data can be traced on how the toughness is affected by molecular and supermolecular variables.

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