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An alternative method was to extrapolate previously published values of 0 shear viscosity to the desired molecular weights and temperatures used in our measurements. However, most data in the literature are on high molecular weight polymers and extrapolation to low molecular weight samples, particularly attempting to account for changes in the glass transition temperature, led to large errors and was not undertaken in this work.
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It is to be noted that the relatively frequency-in-dependent nature of tan δ changes to a decreasing function with reducing frequency at approximately 15.5 and 43.8 rad/s for samples A and B respectively, earlier in time and implying faster response to the network superstructure dominance for sample B. On the basis of these frequencies as corresponding to the frequency where the free chain response is masked by the mesoscale structure, we estimate a length scale of 8.6 and 6.1 nm respectively for samples A and B (considering translational diffusion) as corresponding to the smallest moieties whose relaxation was arrested because of the presence of the superstructure.
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This preconditioning was done to avoid lack of reproducibility and provide a similar initial morphology for each shear rate measured.
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