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Besides, the TiC phase also detected throughout the experiment with increasing in temperature resulting the decrease in number and increase in size.
The movement of the grain boundary has implications for recrystallization and grain growth of alloy.
Other researchers reported that TiC particle was increase in size and decrease in number with the increase in solution treatment temperature [7].
Grain growth take place by the migration of grain boundaries via atomic diffusion across boundary resulting enlarge of grains.
Solution treatment at 1200 ºC shows the austenite grains grow up abnormally to a size of 100.88 μm with decreasing the hamper of grain growth.

The Issue of Increasing the Products Durability Made of Fine-Grain Concrete E.O.
Constant long-term condition monitoring of a number of road surfaces experimental sections allowed to carry out products defects systematization and to classify the reasons of their emergence.
The influence of grain composition of fillers on properties of hard-pressed concrete was estimated at the first stage.
It should also be stopped on the results of the hard-pressed fine-grained concrete corrosion tests with the aim of evaluating the corrosion resistance of fine-grained concrete in conditions of the second and third types corrosion (according to classification of V.
Lotoshnikova, Hard-pressed fine-grained concretes with damping additives, materials of the theses, Rostov-on-Don, 2005

These grain refinements directly affected an increase in mechanical properties.
As a result, the average grain size was refined to 9.8 mm.
Also, equiaxed grains were wholly distributed in the microstructure, including annealing twins in the grains.
In the case of cross-roll rolled materials, more refined grains (average size 6.5 mm) were obtained; these included annealing twins in the grains, as shown in Fig. 1(c).
The Vickers microhardness numbers of the rolled materials were very similar: 127 Hv for the CR material and 124 Hv for the CRR material, as shown in Fig. 3(a).

The number of the passes was 12.
The microstructure investigations of the pointed out samples have revealed a great number of the high-angle grain boundaries and deformation twins in UFGECAP+D+R Cu and the most part of small-angle non-equilibrium grain boundaries in UFGECAP Сu [10].
− is the number of dislocations, blocked at the twin boundary, 3/2 2 )1( fdg!
cTg − = ρ , g − the share of the total dislocation number in the interior grain areas, containing twins, equal to 3/2 2 )1( fdcTg −ρ [9], accumulated at the twin boundaries.
Parameter g which is equal to the total dislocation number in the interior grain areas, containing twins, accumulated at the GB appeared to be 0.224, which corresponds approximately to 2 dislocations.

In this paper, a number of approaches are discussed to control IMC formation in welds between aluminium alloys and magnesium alloy.
(4) where w is the average width of grain boundary, d is the diameter of grains in the direction parallel to the welding interface, and q is a numerical factor depending on the grain shape, q=1 for parallel grain boundaries, and q=3 for cubic grains.
From Fig. 2 (a), all grains of the Mg17Al12 phase (Gamma phase) have a similar grain size, but grain size of the Al3Mg2 phase (Beta phase) is not homogeneous.
For the layer thicknesses and very small grain sizes in the IMC encountered during welding, grain boundary diffusion is thus predicted to dominate.
(a) (b) (c) (d) Figure 3: (a) effect of grain size on grain boundary diffusion, lattice diffusion, and effective diffusion coefficient of the Mg17Al12 phase, (b) effect of grain size on grain boundary diffusion, lattice diffusion, and effective diffusion coefficient of the Al3Mg2 phase, (c) effect of temperature on the diffusion coefficient of the two phases when their grain size is 1 µm, and (d) effect of temperature on the diffusion coefficient of the two phases when their grain size is 10 µm.

The TBRVE consists of a certain number of grains and orientations of the polycrystal, which conveniently represents the global texture and can capture the mechanical response of the material including the BE under cyclic loading.
It is a small volume element which contains a sufficient number of grains to model the global response of the macro-scale specimen.
The EBSD data obtained on the AA7075 specimen is imported to the MTEX toolbox [26] where the ODF is generated, and then crystallographic orientations are obtained by discretising this ODF with the grain number in the RVE as the control parameter.
Before carrying out the simulations, convergence studies in terms of grain number, grain orientation, mesh density and tessellation were conducted to obtain the appropriate RVE.
The model consists of a total number of 51840 brick elements (C3D8R), and the grain tessellations at the edges have been created to be repeatable in each direction.

The overall number of austenite grains decreases and the inhomogeneity of austenite grains increases as some larger austenite grains merge the smaller ones.
The austenite grains spontaneously develop to be less grain boundary area and lower grain boundary energy.
The grain boundaries of austenite are flat and the overall number of austenite grains are few as shown in Fig. 5(a).
Meanwhile, the overall number of austenite grains increases and the grain size of austenite decreases with the increasing of heating rate.
The coarse grains disappear and the percentage of austenite grains with grain size below 20 μm is 79.4%.

With the number of a-Si3N4 grains increased, the weight loss decreased gradually.
With the number of a-Si3N4 grains increased, the linear shrinkage gradually decreased.
Therefore, as the number of a-Si3N4 grains increased, the linear shrinkage decreased gradually.
Although the size of the β-Si3N4 grains was relatively small, the number of the rod-like β-Si3N4 grains with a high aspect ratio was small.
Therefore, the distribution of β-Si3N4 grains size was relatively even, and the number of coarsened β-Si3N4 grains was relatively small.

In order to locate and segment the image of grain bags in the granary reserves, and making full use of the spatial location information of grain bags, a threshold method is proposed base on two-dimensional Fisher criterion.
It is of great practical significance for upgrading the supervision level of grain management.
(3) where, is the integer function, let K that is usually an odd number denote the neighborhood width of pixel (x, y).
In the actual scene of grain bags reserves, the grain bags had the characteristics of relatively consistent, while the gray value of each bag region are concentrated and well-distributed.
In terms of the segmentation results, the traditional 1D Fisher method can segment each grain bag region, but that approach had some segmentation error, caused loss of some grain bag regions.

First, the exponent of the inverse grain size is given by p = 2.
The alloy had an initial grain size of ~1.8 μm after annealing at 473 K for 1 h and was refined by ECAP processing for 8 passes to have a mean linear grain size of ~0.8 μm [8].
It should be noted that the tensile axis is vertical in the micrograph in Fig. 1(b) and the grains appearing white are the Zn-rich grains and the grains appearing dark are Al-rich grains.
The disk samples with a diameter of ~10 mm and a thickness of ~0.80 mm were processed under a pressure of 6.0 GPa at 1 rpm for total numbers of 4 and 5 turns in a constant rotational direction.
There is a reasonably homogeneous distribution of Zn and Al grains with an average linear intercept grain size of ~350 nm.