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Stress dependent variation of (a) number density (b) void diameter (c) void volume fraction (d) void size distribution.
The plot between void volume fraction and number density with rupture ductility is shown in figure 4.
From the fact that the austenite grain size is about 600 mm in the crept microstructure, the aligned voids for the sample crept at 120 MPa, could be interpreted as being interfaces within the grain interior such as packet or lath boundaries.
This is because the spacing between the rows of aligned voids clearly is much less than the prior austenite grain size.
Thus, a transition of cavitation with applied stress during creep in this steel occurs from being predominately restricted at the grain boundary at stresses 150 MPa and above, to progressively proliferate the grain interior interfaces at lower stresses.

Grain growth is observed to be heavily dependent upon twinning processes.
Numbers 1- 3 in bold on the image in Fig. 2 indicate the regions from where recrystallization nuclei were first observed.
The development and migration of the high angle grain boundaries is evident in the maps as the growing grains sweep out regions of high lattice curvature while forming the new grains.
First, a grain is defined in the standard way with EBSD data.
The GOS for each grain is simply the maximum difference in orientation between any two points within a single grain.

The presence of unreacted Si is generally attributed to melting and fusion bonding of Si particles caused by a large number of small particles possessing high reactivity.
These images indicate that the grain shapes of the products can be varied by changing the premixing conditions.
The products synthesized under conditions (b) 0×200 and (e) 135×200 had a large number of rod-like grains with only a few small particles, and the grain size of (b) is smaller than that of (e).
The larger raw particle sizes shown in Fig. 3 resulted in large, uniform rod-like grain shape in the products, while the smaller ones led to small and non-uniform grain shapes which included some whiskers.
Larger raw particle sizes resulted in large and uniform rod-like grain shapes in products, while smaller ones led to small and non-uniform grain shapes, including some whisker-like structures.

The grain size of Number F is smaller than Number E.
The result confirms that PVP influences the grain size of PZT film, and with the increase the amount of PVP in PZT sol, the grain size decreases.
c b a Fig. 7 AFM images of PZT film No additive (a), Number D (b), Number E (c) 4.
Effects of additives on PZT films surface morphology and grain size were investigated.
PVP influences the grain size of PZT film, and with the increase the amount of PVP in PZT sol, the grain size decreases.

This is caused by grain peeling during polishing.
The number of oxygen vacancies generally increases with annealing in vacuum, and these oxygen vacancies promote oxygen diffusion.
In addition, the grain at the triple-phase boundary has the highest contrast.
The depth profile results indicated by Line 3 in Fig. 2 (b) suggest that C[18O] decreased rapidly around the first grain boundary from the surface and reduced at other grain boundaries.
This result indicated that the grain boundary around the surface blocks oxygen diffusion.

Examples are the Grain Interaction (GIA) model [1] that considers geometrically necessary dislocations to achieve strain compatibility across grain boundaries and the full-field Fast Fourier Transform (FFT) model [2].
As all grains are assumed to undergo the same deformation, grain interactions are neglected.
Initial grain boundary orientations are chosen at random.
The VPSC scheme [9] considers the interaction between individual grains and the homogenized medium.
Acknowledgements This research was carried out under the project number M41.2.08307a/M41.10.08307b in the framework of the Research Program of the Materials innovation institute M2i (www.m2i.nl).

The grain size distribution of Ni powder Ni powder grain size [μm] The 1st group 150～155 The 2nd group 70～75 (a) grain size 150～155 μm (b) grain size 70～75 μm Fig.1 The SEM micrographs of porous cermets with different grain size of Ni powder Fig.1 is the SEM micrographs of porous cermets with different grain size of Ni powder.
From the pictures we can see that the bore diameter with grain size 150-155 μm is lager than the bore diameter with grain size 70-75 μm.
Conclusions (1) The bore diameter with Ni grain size 150-155 μm is lager than the bore diameter with grain size 70-75 μm.
(2) The porosity of number one is smaller than number two.
The average porosity of number one is 45%, and number two is 48%

These bands usually transform into grain colonies with a similar orientation during recrystallization in hot strip annealing.
After one-pass ECAP, dense deformation bands were observed as nearly parallel to the shear plane of ECAP inside a number of grains in both the 16 mass%-Cr steels and pure ion.
However, in ECAP process, grains were smaller and equiaxed, and grains with similar crystal orientations were randomly arranged.
The cold-rolled ND//{100} grains embedding the deformation bands became easily recrystallized.
The second possibility is that this deformation band is a grain-scale shear band as a manifestation of plastic instability.

They consist of soft, coarse-grained regions surrounded in three dimensions by an interconnected network of hard, ultra-fine grained regions.
The internal twins in the grains were included in the grain size measurement.
(b), (d): a grain size distribution image.
Grain size: white: < 5 mm, black: ≥ 5 mm.
Acknowledgement This work was supported by JSPS KAKENHI Grant Number JP18H05256 and 18H05455.

However, the number of applications is restricted because they are poor ductility at room temperature, due to the hexagonal close-packed structure and limited independent slip systems.
The reason that tensile properties of 45° samples were better than that of 0° is that slip and twinning were difficult to be activated due to most of grains are hard orientations with low Schmid Factor in 0°samples, while slip can be activated in some grains and twinning can be activated in other grains in 45° samples.
As a result, the proportion of compression twinning and secondary twinning boundary length can not be on behalf of the number of twinning quantitatively.
≥15°grain boundaries; ≥3°grain boundaries; 86°<11-20>tension twinning boundaries; 56°<11-20> compression twinning boundaries; 38°<11-20> secondary twinning boundaries； boundaries between {10-12} twin variants.
Nano grained AZ31 alloy achieved by equal channel angular rolling process.