Page 289 - Engineered Interfaces in Fiber Reinforced Composites
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270               Engineered interfaces in jiber reinforced composites

                    Peters (1982) in that the experimental R-curve is slightly higher for [0"/90"],, glass-
                    epoxy laminates than for  [Oo/ f 45"/0"], laminates in center notched (CN) tension
                    specimens, particularly for long crack lengths. The KR values are compared in Fig.
                    6.25 between the two laminates with different layup sequence. The ever-increasing
                    R-curve for Kevlar fiber composite laminates with all layup sequences is due to large
                    fiber pull-out lengths and damage zone size. Thinner specimens normally give higher
                    R-curves in SEN tension  tests of laminates (Solar and Belzunce,  1989), and short
                    fiber composites (Aganval and Giare, 1982).

                    6.4.3.2. Fracture process zone or damage zone
                      The  R-curve study normally  involves the characterization  of critical  size of the
                    FPZ or damage zone, CO, at the crack tip region, which is analogous to the approach
                    used for predicting the plastic zone in metallic materials. The damage zone is directly
                    responsible for the increasing crack growth resistance, R-curve, behavior  observed
                    in composites  whether  the direction of  loading is  along  or transverse to the fiber
                    direction  (i.e.  interlaminar/intralaminar  or  transverse  fracture).  The  damage  in
                    transverse  fracture  of  composites,  as  schematically  shown  in  Fig.  6.17,  can  be
                    divided into two regions:
                      (1)  the damage zone ahead of  the advancing crack  tip where matrix  cracking,
                          interfacial debonding, post-debonding friction occur;
                      (2)  the fiber bridging zone or tied zone at the wake of the crack tip where fibers
                          bridge the opposite fracture surfaces and pull-out.
                      The  size of  damage  depends  on fiber  6, fiber  aspect  ratio,  types of  fiber  and
                    matrix material, bonding at the fiber-matrix interface, layup sequence in multi-angle
                    ply  laminates,  specimen  geometry  including  laminate  thickness,  and  loading






















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                    Fig.  6.25. Maximum  fracture toughness, KR, as a  function  of  relative crack length,  2a/W, for carbon
                        fiber-epoxy matrix [O"/ * 45"/O"],  and  [0"/90"],, laminates. After Ochiai and Peters (1982).
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