Abstract. The notion of Lipschitz p-summing operator is introduced. A nonlinear Pietsch factorization theorem is proved for such operators, and it is shown that a Lipschitz p-summing operator that is linear is a p-summing operator in the usual sense.

Internal fixation for bone fractures with rigid metallic plates, screws and pins is a proven operative technique. However, refracture's have been observed after rigid internal fixation with metal plates and plate fixation has been known to cause localised osteopenia under and near the plate. In the present study, resorbable composites comprising a PLA matrix reinforced with iron doped phosphate glass fibres were investigated. Non-woven random mat laminates of approximately 30% and 45% fibre volume fraction (V(f)) were produced, along with unidirectional and 0°-90° samples of approximately 20% V(f). The non-woven composite laminates achieved maximum values of 10 GPa modulus and 120 MPa strength. The 0-90º samples showed unexpectedly low strengths close to matrix value (~50 MPa) although with a modulus of 7 GPa. The UD specimens exhibited values of 130 MPa and 11.5 GPa for strength and modulus respectively. All the modulus values observed were close to that expected from the rule of mixtures. Samples immersed in deionised water at 37°C revealed rapid mechanical property loss, more so for the UD and 0-90º samples. It was suggested that continuous fibres wicked the degradation media into the composite plates which sped up the deterioration of the fibre-matrix interface. The effect was less pronounced in the non-woven random mat laminates due to the discontinuous arrangement of fibres within the composite, making it less prone to wicking. Random mat composites revealed a higher mass loss than the UD and 0°-90° specimens, it was suggested this was due to the higher fibre volume fractions of these composites and SEM studies revealed voidage around the fibres by day 3. Studies of pH of the degradation media showed similar profiles for all the composites investigated. An initial decrease in pH was attributed to the release of phosphate ions into solution followed by a gradual return back to neutral.

We examine some structural properties of (injective and projective) tensor products of ^-spaces (projections, complemented subspaces, reflexivity, isomorphisms, etc.). We combine these results with combinatorial arguments to address the question of primarity for these spaces and their duals.Introduction.

The thermal conductivity of a thermosetting advanced composite material during its cure was experimentally investigated and compared to analytical models. The thermal conductivity of graphite/epoxy was experimentally measured using a guarded hot plate apparatus. The through-thickness transverse thermal conductivity of composite laminates was measured at various resin degrees of cure and fiber volume fractions while using various ply lay-up angles. The in-plane thermal conductivity was measured using unidirectional laminates, as well as laminates with various ply lay-up angles. Techniques for manufacturing composite laminates with these various properties, as well as the guarded hot plate apparatus necessary for accurate measurements, are described. Finally, various analytical models were researched, and those that compare most favorably with the experimental data are presented. NomenclatureH c = thermal contact conductance of the experiment, W/m 2°C H r = resin heat of reaction for AS4/3501-6, J/g K = thermal conductivity, W/m°C L = laminate dimension in the x direction, m N = number of plies in a laminate p = function of the fiber volume fraction, Eq. (6) Q = total heat flux, W q = heat flux/area, W/m 2 q = resin energy generation rate per unit volume, W/m 3 q ln = heat flux/area applied by the guarded hot plate, W/m 2 T = temperature, °C t = laminate dimension in the z direction, m V = volume fraction of a constituent material W = laminate dimension in the y direction, m *, v, z = laminate coordinates defined in Fig. 1 a = resin degree of cure, scale of 0-1.0 y = function of material conductivities, Eq. (11) 8 = resin rectangle side parallel to measured K, fjun e = resin rectangle side J_ to measured K, /mi 0 = direction of ply alignment, Fig. 1, deg v' = function of material conductivities, Eq. (5) p = density, g/m 3 Subscripts act s= actual material property c = experimental setup contact region property comp = composite property

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