We regret that an error during revision and imposition resulted in an unacceptable quality of reproduction for Figs. 7 and 8 of the above paper. Improved versions of these gures appear below. a b c d a P15 composite, crack propagates by ductile voiding in matrix; b P25 composite, similar mechanism as for P15, but broken particles (indicated by arrows) are found; c A30, micrograph taken ahead of the main crack, in process zone: dominant fracture micromechanism is particle cracking (voids are arti®cially enhanced for clarity); d A5, particle cracking and matrix voiding (some broken particles are indicated by arrows) 7 Optical micrographs of crack path of arrested chevron-notch test showing dominant fracture micromechanisms
Al ± 2 wt-%Cu composites were produced by gas pressure in® ltration of powder beds with a high volume fraction (45 to 60 vol.-%) of angular or polygonal alumina particles. The tensile behaviour and fracture toughness of the composites were characterised in as cast, solutionised and peak aged (T6) conditions. It was shown that coarse intermetallics that are formed during solidi® cation and located preferentially at the particle/matrix interface lead to lower toughness compared with the same composites in solutionised and T6 conditions. The particle nature and shape exert a strong in¯uence on the properties of the composites: polygonal particles are intrinsically stronger than angular particles and yield stronger, tougher, and more ductile composites. Composite toughness variations are explained in terms of fracture micromechanisms.MST/5330
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