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The number of the defects in inner side was 1.5~2 times of that in outer side.
By this way, the defects number and location in whole plate were gotten.
(a) grains in slab (b) grains in hot-rolled plate Fig. 3 The grains in slab and hot-rolled plate Fig. 5 showed the distribution of the defects detected by ultrasonic test in the surfboard.
The number of the defects in inner side was 1.5~2 times of that in outer side.
The number of the defects in inner side was 1.5~2 times of that in outer side

As a result, we have achieved a higher VOC of 0.725 V, confirming that the sintering behavior (grain growth and/or necking of grains) influenced largely the characteristics of DSSCs.
It also indicates the promotion of grain growth.
As to the photocurrent, the grain growth is not always favorable for the cells because the amount of adsorbed dye is largely decreased.
In the films heated at the higher temperature, the grain growth proceeded with the necked particles approximately 100 nm in size.
In contrast, VOC increased with the heating temperature probably because of the smaller number of recombination sites on the surface or at the grain boundaries.

Similar results concerning Journal Title and Volume Number (to be inserted by the publisher) 3 misorientation inside the {111} <112> and {111} <110> grains, have already been reported from EBSD measurements by Lesne [4] for a 70% cold rolled ultra high purity iron and by Thomas et al
c d b a 9° 3° d c Journal Title and Volume Number (to be inserted by the publisher) 5 Fig. 5 Cell coalescence in a {111}<110> grain after 2 min annealing at 700°C.
(Arrows indicate the bulging in the neighbouring {110}<112> grain; dashed arrows indicate the growth in the "parent" grain).
Generally, the subgrains located inside the grains or at the grain boundary mainly grow inside their "parent" grain.
After cell coalescence or not, subgrains located near grain boundaries grow, either towards the interior of the "parent" grains, or in the neighbouring grain by bulging, even both.

[4] probably were the first to clearly point out that β solidifying alloys offer significant potential for grain refinement, because in the β/α transformation 12 orientations of α precipitates can be obtained from one parent β grain.
Despite this clear result B could also effect grain refinement during solidification, e.g. at higher concentrations of B and Al.
The interdendritic regions contained Borides and in some cases single-phase γ grains.
Similar refined microstructures could also be achieved in this work in quite a number of alloys containing (44 - 45.5) at.% Al, (0.1 - 0.2) at.% B, (5 - 8) at.% Nb and additions of Mo, W or Fe up to 2 at.%.
After this heat-treatment the alloy showed a microstructure consisting of α grains with a size 0.5 - 1 mm (Fig. 3).

The grain of graphite consists of a stack of parallel hexagonal net planes as schematically shown in Fig. 1.
(3) It is assumed that the crack will extend at a grain size, a, if the entire low with n grains fail.
When N is the number of pores per unit volume and V is the specimen volume, the total survival probability of the volume V under stress σ having 2NV flaw tips is (Ps) 2NV.
Input parameters such as pore size, grain size etc. are required in the analysis same as the uniaxial ones.
Fig. 3 Analytical flow of strength prediction under multiaxial stress Table 1 Input parameters of PGX graphite [8] Parameter Value Mean grain size (μ m) 762 Bulk density (g/cm3) 1.74 Mean pore size (μ m) , S0 238 Standard deviation parameter of pore size, Sd 1.73 Number of pores per volume (m-3) 0.187x10 8 Grain fracture toughness (MN/m3/2) 0.225 Results and discussions Biaxial strength prediction.

The results show that at 1300℃ a large number of CAS2-Al2O3 caking formed the basic skeleton and some particles were not condensed.
At the same time, little Al2O3 grains are precipitated.
When the holding time extends to 1h, a large number of particles are formed and bonded, the sample porosity reduced and the density increased.
For 4h, the crystal boundaries intersect with each other, the caking body is evener, and a large number of Al2O3 is precipitated.
When the rate reaches 4℃/min, crystal grains are even and clear; grain interaction bond is close, but the blowhole rate increases.

Slope of grain.
Measurement of the slope of grain.
Mean density values ρm [kg/m3] and variation coefficient values CV [%] according to the grading criteria Number of accepted beams Criteria applied ρm CV [%] 45 (100%) None 680 10.04 40 (89%) Knots and slope of grain 679 10.28 35 (78%) Knots, slope of grain and insect attacks 685 10.24 Modulus of elasticity.
Number of accepted beams Criteria applied fm fm,k (5º percentile) CV 45 (100%) None 38 20 31.30 40 (89%) Knots and slope of grain 41 26 27.34 35 (78%) Knots, slope of grain and insect attacks 43 29 18.90 Strength class according to the results.
Number of accepted beams Criteria applied fm,k Eg, mean ρmean 45 (100%) None 20 13.565 680 40 (89%) Knots and slope of grain 26 13.976 679 35 (78%) Knots, slope of grain and insect attacks 29 14.484 685 Wood boring insect attack.

In many applications, such as milling or percussion drilling, they are subjected to fatigue with considerable loading cycle numbers.
Thus S-N curves (so called Wöhler plots) are determined to limited number of loading cycles < N= 107.
The data indicate a continuous decrease of fatigue life without any horizontal section even up to 1010 number of loading cycles.
Fig.5: Normalized S-N curves of hardmetals with 10% Co content and grain sizes of 2µm and 0,4µm Fig. 6 shows as an example the pronounced influence of residual stresses on fatigue life which decrease with increasing number of loading cycles, possibly due to changes in fracture morphology.
Both curves are steadily decreasing, and pronounced difference was observed between the stress amplitudes of the two curves at 107 numbers of cycles.

The grains in the C2 condition were finest.
The Al concentration in the grain boundary precipitate was five times as high as in the grains.
Zn was not detected in the grains while there was a great amount of Zn in the grain boundary precipitate.
Thus, we found that a number of solute atoms were segregated into the grain boundary.
In C1 condition the secondary phase of about 5 wm size was distributed in grain as well as grain boundary, while in C2 condition the phase of 10 wm was limited just to the grain boundary.

The volume fraction of high-angle grain boundaries was about 57%.
However, the number of superplastic aluminum alloys is currently limited because of difficulties in producing an ultra-fine grain structure by conventional routes of thermomechanical processing [1].
The ultrafine grained structure stabilized by these nanoscale dispersoids is stable against grain growth under superplastic conditions [9,10].
In addition, grains tend to elongate along tension direction.
The uniform fine grain structure is necessary for frequent operation of GBS by shifting of the grain groups along the common grain boundary surfaces [1, 16].