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Whereas, the compaction wave formed following the elastic precursor was propagated at a constant velocity much slower than the elastic precursor.
Inertia stress calculations shows that the fast moving elastic precursor is reflected from the distal end and reduces the inertia component of the total stress.
It was observed that an elastic precursor propagates, at a velocity of 740 m/s, along the material upon impact, and it decays as it propagates along the specimen.
Twinning area fraction and dislocation density are higher at the impact surface region than at the back surface due to decay of the elastic precursor and the difference in loading duration.
In particular, we find that the elastic shock wave can readily trigger the α→ω transformation at {10¯12} CTBs but not the other two GBs, and the α→ω transformation at CTBs leads to considerable wave attenuation (i.e., the elastic precursor decay).
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Observations of the grain boundary region showed that a smooth transition occurred between the elastic precursors in both grains as well as the plastic waves (when plastic flow is evident).
The uniaxial stretching of hard elastic HDPE precursor films induces the bending of crystalline lamellae, which leads to the formation of micropores between them.
It is found that the magnitude of the outer wall motion due to the precursor elastic waves is small, while the associated wall motion is unsteady and decays in amplitude as the elastic disturbances move further ahead of the detonation front.
The motion of the outer Al wall due to precursor elastic waves in the Al running ahead of the detonation is also measured at various axial locations along the cylinders.
The development of hard elastic high-density polyethylene (HDPE) precursor films and its influence on the microporous membrane formation have been investigated.
The coatings prepared from more concentrated solution precursors had average elastic modulus and hardness nearly two times greater than the coatings prepared from solution of low concentration.
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