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The numbers in (b) refer to grain orientations analyzed via EBSD (Table 1).
The numbers in (b) refer to grain orientations analyzed via EBSD (Table 1).
The numbers in (b) refer to grain orientations analyzed via EBSD (Table 1).
However, there were a number of significant differences.
The CA model successfully reproduced a number of the features of the DDRX and MDRX for Waspaloy ingot material.

The wear tests showed that the wear weight loss curve of Hadfield steel will be bent down after some critical impact numbers.
The wear curve of the AISI 1045 steel, however, shows a step-like characteristic with increasing impact numbers.
Grain size of ferrite is about 10~12 µm.
Finally, nano grains are formed in subsurface.
The "white layer" with nano grains does not.

The results show that the mechanical properties of coarse-grained materials are more strongly affected by the current pulses than finer grained material.
In pure Mg, twins formed inside the grains.
Still, the number of twins was very low in comparison to pure Mg.
With the higher current density, similar to pure Mg, wide twins formed inside the grains.
The higher drop in stress in the plastic regime can be explained by the interaction between electrons and the larger number of dislocations.

As illustrated in Fig.1(b), the size of the core layer grains was about 200μm and these grains were almost equiaxed ones.
However, a small number of core layer grains were still at the elongated state because the silicon content of the core layer was high and the full recrystallization energy was not enough.
These stripes were similar to sub-grains and the grain boundarys were shallow and blurred.
In Fig.2(f), a large number of holes could be seen from the microstructure of furnace-cooled composite plates’ core layer, which implied that silicon loss was severe during the slow cooling in high temperature.
The core layer grains grew up sufficiently.

The forces acting on individual grains, among various factors affecting wheel wear, play a very important role since they dominate grain fracture and grain pullouts from the bonding [1].
A commonly used method for estimating such forces is to divide the total tangential and normal forces by the number of active grains in the contact zone [3].
It is apparently more reasonable to use the maximum forces along the path instead of the average value for evaluating grain fracture and grain pullouts.
The maximum forces on individual grains can be calculated as the peak distribution value divided by the number of active grains in the area of grinding width by a unit arc length.
To predict force distributions, the full arc B0T0 is divided into consecutive segments or sub arcs: s1, … si, … sN, where N is the total number of segments.

The second order stresses characterize the deviation of the stress in a particular grain from the first order value.
On the grain-scale, plastic deformation occurs due to the dislocation slip on crystallographic planes.
The second term of Eq. 3 describes the interaction stresses created due to differences between the sample and grain deformation rates (incompatibilities of grains with the surrounding aggregate).
We can see that the maxima of ODF correspond to the lowest or medium values of grain stresses, while the highest stresses are found for some orientations related to low number of grains (low values of ODF).
Low incompatibility stresses are generated in grains having preferred orientations.

The Si3N4 porous ceramic contains a plurality of Si3N4 crystal grains with pores formed in grain boundary which forms a three-dimensional network structure.
A number of patents describe the preparation of porous silicon nitride ceramics since the 1980s, such as a porous silicon nitride ceramics can be prepared by adding gypsum or coarse silicon powder to the raw materials [1,2] and Matsuura et al. got porous silicon nitride ceramics by adding rare earth oxides to the raw material of the silicon nitride [3].
Fig.5 shows that the silicon nitride porous body comprises a body part and a pore part, where in the body part is formed by a plurality of b- Si3N4 crystal grains, the silicon nitride crystal grains with pores formed in grain boundary which forms a three-dimensional network structure.
Large aspect ratio b-Si3N4 grains may be easily formed, which can be seen in Figure 7.
(4) Large aspect ratio b- Si3N4 grains may be easily formed at vacuum furnace, compared with at Nitrogen atmosphere pressure furnace.

Only a limited number of probes is available to determine the how the material behaves under these dynamic loads.
The microstructure did not have a significant texture, and the departures from perfectly random orientation can be attributed to the statistics resulting from a fairly small number (a few tens) of larger grains.
The grains are largely free of dislocations and other defects, apart from the grain boundaries.
Like any rigid body rotation, the lattice orientation is specified by three numbers, often expressed in terms of Euler angles [55].
The number 8 is chosen to equal the number of nearest neighbors in the strain-free perfect bcc lattice, and this number would be different in different lattices.

The properties of welded joint will been improved by these fine crystal grain.
Following the increasing of magnetic field current, the numbers of α-Mg are increasing and display as equiaxed grain, the β-Al12 Mg17 are diffusion distribution at the grain boundary of α-Mg, showen in Fig.4 b).
The grain consist of coars α-Mg and series β-Al12 Mg17.
These broken crystal grains can refine grain and improve the properties of welded joint.
The properties of welded joint will been improved by these fine crystal grain.

When rolling in the unrecrystallized zone, a large number of defects such as sub-grain boundaries, dislocations, and deformation bands are formed in the material.
These defects can become ferrite nucleation points, which greatly increases the number of ferrite nucleation and suppresses the growth of grains, to realize the grain refinement strengthening.
Through continuous large deformation at high temperature and strain accumulation, hardened austenite containing a large number of "defects" such as grain boundaries, sub-grain boundaries, and dislocations is obtained.
In order to reduce the interfacial energy by reducing the grain boundary area, the flat ferrite grains formed by rolling deformation have a tendency of spontaneous transformation to equiaxed grains.The total grain boundary area of the web sample is larger than that of the flange and R angle ,because the web is flat and its grain size is smaller than that of the flange and R angle sample.
Since the macroscopic plastic deformation of flat grains is slightly smaller than that of equiaxed grains of the same size, the average impact energy at the flange is slightly higher than that of the web, while the grain size at the R angle is larger, and due to the different rolling directions, there are obvious mixed crystals, the distribution of instantaneous deformation is not uniform, the large-size grains yield preferentially, while the small-size grains have not rotated yet, and the strain difference between the two sides of the grain boundary has increased significantly, which is most obvious at the three grain boundaries.