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Each place food source (position) only one leading bee, that is to say the food number and lead the number of bees equal).
In the grain area, the sensitivity of the human eye is higher than the edge of no edge area, but below the smooth area.
Thus, we will be a visualization is divided into three areas: smooth area, edge area, grain area.
When the P value more hours, in the stable region, when P is opposite bigger, in the grain area, when P is very large, it is in the edge area.
Avi (frame number for 352), the platform is the size of the watermark vc6.0 (20.

Theory foundation of BSE experimental study It is obviously to find different shading from back-scattering micrograph when D-value of average atomic number of two material is bigger than 0.1.Through our research and analysis of previous experiments[10], average atomic number of two elements in cement differ apparently.
Experiment indicates, because atomic number (Z=97) is the highest, the influence to image contrast is enormous.
Cement powder condition includes Fineness control values (specific area and residue on sieve), particles morphology and grain composition.
It provides a large number of experimental data for micro powder performance study.
Calculation and analysis process indicates that: BSE image contains large information, not only the comprehensive grain composition and microstructure, but also each composition’s grain composition and microstructure and so on.

IN-738, have been observed coarse γ΄ particles surrounding by small in size of γ΄ particles and also continuous M23C6 carbides along grain boundaries of γ matrix [5–7].
The results of number density of γ΄ particles per area in μm2 are plotted in Fig. 3.
However, a slight reduction in the number of γ΄ precipitates per area with the increase in aging time can be seen.
Only the sample in program C1 presents a significant decline in has the number γ΄ precipitates per area in comparison with that of the sample C2.
Koo, Effect of Solution-Treatment on Microstructure and Mechanical Properties of Cast Fine-Grain CM 247 LC Superalloy, Mater.

The grain size of the material varied from 200 up to 600 µm.
The microstructures contain deformation twins, the number of which increases drastically at high strain rates.
The heavily twinned grains show higher hardness than the less favorably oriented and only lightly deformed grains, as reported also by other researchers [6].
Thus, the twinned grains that are more frequent at high strain rates are most likely the cause of this effect.
At high strain rates, the hardness is locally more concentrated in the twinned grains, which also shows as the different frictional behavior of individual grains.

The surface morphology of Ni-SiC nano composite prepared under ultrasonic stirring exhibited pronounced smooth surface and finer grains as compared to the composite without ultrasonication (US) (Fig.1a&b).
As it can be observed from the surface morphology that the Ni-SiC composite coating prepared in ultrasonic condition is more compact and consists of smaller and round grains (Fig.1b).
Microhardness of the metal nano composites is mainly affected by three factors; particles hardening, dispersion hardening, and grain refining.
During the ultrasonic electrodeposition, both grain refining and dispersion strengthening affected the increased microhardness.
The enhanced microhardness of Ni-SiC composite with smaller particle size in the deposit was also attributed to the increasing values of the number density.

The former can only get the total conductivity of the material, while the latter can separated the contribution of the grain, grain boundary and electrode from each other, so as to get the grain conductivity data which reflects the intrinsic characteristics of the material.
From AC impedance spectroscopy as shown in Figure 3, we can get the grain resistance and grain boundary resistance (Rg+Rgb) together.
Under normal circumstances, an ideal impedance spectra of the solid oxide electrolyte material is mainly composed of three semi-circles which we called Cole-Cole, here we only get part of Cole-Cole, the reason is that semi-circle number depends on many factors such as material, test temperature and frequency range etc.

The chemical potential gradient associated with a curved interface is such that, due to statistical thermal fluctuations, large precipitates will tend to grow and small ones to dissolve, leading to a decrease in the number of particles [1].
(c) (b) (a) Fig. 1. γ` images of (a) as-received and thermal exposed specimens for 10,000 hrs at (b) 871 oC and (c) 982 oC Figure 2 shows grain boundaries and their surroundings of as-received and thermal exposed specimens for 10,000 hrs at 871 oC and 982 oC.
In the case of as-received specimen (Fig. 2(a)), Ta and Ti rich carbide are located along grain boundaries.
The grain boundary area of thermal exposed specimen at 982 oC can be compared with as-received.
As shown in Fig. 2(b) sigma phases around grain boundary were observed after thermal exposure at 871 oC.

As shown in the case of '100' dwell time, both number and size of cavities of cavities increased.
As shown in Fig. 7, cavities were observed along PAGB (Prior Austenite Grain Boundaries), and this intergranular damage is caused by cavities during the dwell period.
This result indicates that material degradation becomes more prominent as more cavities form along grain boundaries by the increased effect of creep during dwell time.
(a) cavity at prior austenite grain boundary (b) high power view of (a) Fig. 7 Crack growth path and cavity at prior austenite grain boundary ( dwell time: 1000s) Conclusion From the above experimental results obtained with both P92 HAZ and base metal, following conclusions were obtained.
As the dwell time increased, microvoids /cavities and microcracks that formed along the prior austenite grain boundaries ahead of the main crack contributed to the intergranular crack growth, and the fracture mode was intergranular by the effect of the creep generated during the dwell time.

Although powder and solid-form of zirconia has been widely investigated in terms of grain sizes and crystalline phases, phase transformation energetics, particle morphologies [5-6], etc, these properties were rarely reported on nanofibrous zirconia materials.
Precursors with additional 100% deionized water, 110% deionized water and 120% deionized water were numbered as F2, F3 and F4, respectively.
Fig.2 SEM of F2 Fig.3 SEM of F2 (800°C treatment) Fig.4 SEM of F3 Fig.5 SEM of F3 (800 °C treatment) Fig.6 SEM of F4 Fig.7 SEM of F4 (800°C treatment) Fig.8 Bar chart of average diameter X-ray diffraction and grain size of nanofibers XRD curves for nanofibres heat treated at 200°C and 800°C were given in fig.8.
We can see the zirconia grains clearly, the grain size at about 30nm to 40nm, after heated treated at 800°C, see fig.9.
There were ZrO2 crystalline with tetragonal phase when the fibers were heat treated at 800°C and the grain size at about 30nm to 40nm.

In Fig.1 (c), it can be obviously seen the phenomenon of grain boundary nucleation of BF.
The white arrow points out the γ grain boundary. 1, 2 denote that BF formed at different locations along the grain boundary.
Several BF nearby start from grain boundary and nearly parallel grow to the same-side γ.
Then lamella thicken, contact and elongate longitudinally ending at the grain boundary or another BF lath like 1, 2 noted in Fig.1 (d).
Fig.1 (e), (f) shows that the number of BF lath beams parallel to each other increase during 36, 48 h isothermal treatment.