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The pronounced reorientation of cross-linked epoxy resin melts can be ascribed to the inter-bonded chains.
Consequently, strain-softening of diblock copolymer melts can be tuned by the weight/volume ratio of the two blocks.
It has been concluded that die drool phenomenon of HDPE polymer melts can be explained by the flow induced molecular weight fractionation.
It is studied how much widely the microscopic compositional distribution in SiGe multicrystals grown from binary Si Ge melts can be controlled by the melt composition and the cooling process.
Since the synthesis of block copolymers with a narrow polydispersity and a wide variety of backbones such as a rod-coil or a coil-coil block copolymer has undergone considerable development over the last 20 years, the morphology of self-organized nanostructures in block copolymer melts can be controllable from the viewpoint of polymer design and treatment conditions generating the desired phases.
Here we provide conclusive evidence that the shape of the phase diagram is determined primarily by the ratio of the chain length of the polymer melt to the chain length of the polymeric shell structure (or hair) of the core/shell nanoparticles, and that the phase behavior of different hairy particles in various polymer melts can be superimposed into one universal graph.
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This melting can be a problem, particularly if the melting ice starts its life on land.
The magnitude of glacier melting can be seen at the Rongbuk glacier on the northern slope of Mount Everest.
From this result, the solidification front of melt can be decided.
The crystallization kinetics of the metastable melt can be determined by means of differential scanning calorimetry.
This difference in melting can be accounted for by modulating the ablation factor according to debris properties.
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