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These metallographic shows M7C3 grains become larger when the distance is increasing from the fusion line.
Then, different grain began to form in the surfacing layer.
A large number of carbides began to form at the same time.
This is because a large number of M7C3 and TiC ceramic hard phase were formed in the surfacing layer.
The concentration gradient of C between the surfacing layer and base metal is big, because Fe-Cr-Ti-C alloy contains large number of C.

It is indicated that the average Nusselt number showing an undershoot during the transient period and that the time needed to reach the steady state is longer for low Rayleigh number and shorter for high Rayleigh number.
This interest was estimated due to many applications in, for example, packed sphere beds, high performance insulation for buildings, chemical catalytic reactors, grain storage and such geophysical problems as frost heave.
Variation of the transient average Nusselt number with s at different Rayleigh number.
This variation of the transient local Nusselt number is reflected on the average Nusselt number.
Fig. 4 shows the variation of the average Nusselt number with the dimensionless time for different Rayleigh numbers.

Because the initial inelastic scattering generates electrons with a continuous range of directions, a number of planes fulfill the Bragg condition.
The orientation and grain size of each grain were determined by EBSD measuring system.
The grain size was defined by a diameter of the circle that has the same area of a particular grain.
EBSD pattern was generally measured at the center part of grains.
All SEBSD are evaluated at the center of grains.

This fact was supported by a number of AE detected in this period.
The number of Type-B AE increased stepwise, while Type-A AE increased at around 10 ks after Type-B increased.
We observed falling-off of grains along the surface SCC, as shown in (c).
This was formed by falling-off of the grains and not by anodic dissolution.
dissolution along chromium depleted grain boundary.

This means that the fraction of high-angle boundaries in the subgrain structure of given size, which can well be estimated as fhab = w/d [30], may be varied by varying the number of passes.
The minimum ε& min of creep rate increases by orders of magnitude as the number of passes goes up from 2 to 8.
Fig. 4.Modeled steady state deformation resistance of Cu in dependence of grain size d; d = 50 µm: conventional grain size; d ≤ 1 µm: "small" grains.
Fig. 4 illustrates the grain size dependence of the steady state deformation resistance of Cu with "small" grains in comparison to conventional grains.
"Small" means that the dislocations are stored at the grain boundaries only, not within the grains.

At a low value of Z abnormally large grains formed during annealing.
Although a number of studies have been undertaken on the static recrystallization of cold rolled interstitial free steel [e.g. 2-5], there is only minor reference in the literature to the recrystallization behaviour following warm working.
The average linear intercept ferrite grain size thus achieved was 25µm [10].
After 30 s a few new strain free grains can be observed.
In Figure 4c a number of the large apparently recrystallized grains contain, in their interior, a few low angle boundaries.

Polycrystalline laser hosts have a number of advantages compared to single crystals, including higher dopant concentration, cheaper fabrication, and larger devices.
A number of studies have shown that microwave heating often results in superior microstructure with fewer trapped pores, cleaner grain boundaries, and smaller grain size than traditionally sintered materials.
The figure shows the larger micron-sized yttria grains surrounded by the submicron-sized alumina grains.
The grain structure appeared to be 2-5 µm.
The grain boundaries appear to be clean, although there are a number of trapped pores [see Fig. 3(c)].

Misorientation Effects on Grain Boundary Grooving of Ni by Liquid Ag P.
On the contrary, GB energies vary in a very wide range depending on grains misorientation and plane position.
Grain size about 100 - 200 µm was obtained.
Randle: The Measurement of Grain Boundary Geometry (IOP Publishing, UK 1993)
Nevertheless, the study of a large range of GBs geometry required the use of a great number of different bicrystals.

The results indicated that Al microparticles slowly dissolved into nickel grain to form an ultrafine-grained Ni3Al/NiAl composite with micro-sized pores dispersion due to volume shrinkage.
After 3h annealing, both the number and size of black Al microparticles significantly decreased, but gray areas with micro-sized voids dispersion around Al microparticles appeared, as seen in Fig.2c.
From Fig.2d, it can be found that the grain size increased to the averaged ~220 nm.
Thus, the number of alumina nuclei formed on the A-EMC Ni-Al increased with the increasing of annealing times.
In another word, the number and size of voids gradually decreased with the increasing of annealing time, as seen in Fig.2.

Recently, a large number of researches focus on Bi0.5Na0.5TiO3 (BNT)- and K0.5Na0.5NbO3 (KNN)- based lead-free piezoelectric ceramics[2].
To improve its piezoelectric properties, a large number of BNT-based solid solutions, such as BNT-Bi0.5K0.5TiO3 [4], BNT-NaNbO3 [5] and BNT-Bi0.5K0.5TiO3-BaTiO3[6], have been studied intensively.
Obviously, a preferred grain orientation of (h00) happened.
The vacancy and chemical deviation would hamper the orientation of grains.
In the early period, a large number of grains with a small size could be observed except for some templates with a large size, which proved that the growth of matrix powders along the templates did not take place sufficiently.