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The remaining transformation strain along the β/α″ interface was found to be accommodated by Type 1 twinning on (111)α′′ with Burgers vector bLIS close to ⟨¯2¯13⟩α"(≡⟨¯2¯13⟩αβ).
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The twinning with (10¯1) twinning plane is observed in the orthorhombic M7(C, B 3 (M = Fe, Cr, Mo) phase.
In addition, it is shown that growth of γ-massive domains from their initial nucleus always involves successive {1 1 1} twinning.
The tensile deformation involves the reorientation of (0 0 1) twinning domains, formation of (1 0 0), (20¯1), and (¯1¯13) deformation twins, and detwinning of the existing (0 0 1) twins.
In the alloy studied, deformation twinning was observed, consistent with being the mode of lattice-invariant deformation, and this can occur on either of two crystallographically equivalent conjugate {101}⟨10¯1⟩ twinning systems: conjugation boundaries separate regions within a single variant in which the active modes were distinct.
We also show that the increases in the yield stress and hardening rate with the addition of Al is a consequence of increases in the resistances to slip but a decrease in the resistance to {10¯12}⟨10¯1¯1⟩ twinning.
Figure 1 Twin block appliance in place.
The (1 0 0) twins and the (20¯1) twins grow one by one and form a zigzagged configuration.
These features are kinks and other irregularities in (1 2 0) twins, and V-shaped indentations on (1 2 0) and (1 2 2̄) twin planes.
The occurrence of the {1 0 ¯1 1} twinning at Type II intersections suggests an inclined twinning shear mechanism.
In this thin film the thermally formed martensite has (0 0 1) twinning as its substructure due to the effect of Guinier Preston zones.
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