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Because ultrafine ceria grains were easily condensed into clusters, low concentration of abrasives is preferable to Fig. 9 Photographs of burned wheel (type D) and wafer 0 30 60 90 120 150 180 Type A Type B Type C Type D CMG wheels Dressing interval [min] Fig. 7 Typical wafer surface topography after Fig. 8 Effects of wheel types on CMG using Type A wheel (Ra: 0.7nm) dressing interval prevent ceria abrasives from conglomeration.
Fig. 10 SEM image of type B wheel Fig. 11 SEM image of type D wheel With ceria concentration increasing, the number of the effective ceria abrasives (abrasives exposed or released from the CMG wheel) in CMG process did not increased or at least did not increased sharply due to poor self-dressing ability.
(2) The additive of sodium carbonate could effectively weaken the adhesion between ceria grain and bond, resulting in good self-dressing ability to facilitate the chemical reaction between Si material and ceria during CMG process

According to investigations by previous researchers, these oxides are attached to the boundaries of large grains or they are present as small grains [14,15].
This result is quite satisfactory since the increasing number of sodium titanate formed as an intermediate phase is highly expected.

Segregation induced by neutron irradiations causes Cr-depletion at grain boundaries [6, 7].
Low (Cr)/high (Ni,Si) material simulates the grain boundary composition of irradiated 304L type stainless steel.
The number of secondary cracks is very limited Fig. 9 In-situ observation In-situ observation.

The cylinder was assembled by a number of cylinder units linked by flanges.
In the meanwhile, fine-grained and low density ore slime and parts of fine diaspore can move upward with the water flow, the slime was resisted by the Z-shaped inclined plate, the flow turbulent fluctuation was weakened and the rotational motion was turned into upwelling along the inclined plate.
From the radical results of section speed distribution, it can be concluded that high speed appears around the rotator and the speed become gradually weak when flow through the tilting plates, which is contribute to the settlement of the fine-grained grade materials and radical split.

Result and Discussion Fig 1(a) and fig 1(b)are topographical and phase images of SEBS/A187/Si, we could find that the films were smooth and isotropy made by SAM procedure, the micro grains on the topographical images were homogeneously distributed.
Fig 2 present topographical and section images of DLC/SEBS/A187/Si, and the size of its micro grains was 20 nm and the surface roughness Ra=0.56 nm.
The wear trace was shown in fig5, where there were a number of grooves on the surface.

In order to carry high critical current density, superconducting thin film must be well textured to minimize weak links at high-angle grain boundaries [1].
A large number of materials have been investigated for a possible buffer layer on top of the MgO.
From the cross-sectional SEM image, BZO film has a columnar structure which reflects grain growth direction of columns is perpendicular to the MgO substrate.

The upper is red massive fine grained feldspar sandstone, medium to intensity weathering.
The bottom is brownish red thick-bedded fine-grained feldspar sandstone.
Table 3 The indoor shear experiment result of landslide face soil Soil Values Quick shear Repeated saturated shear C[kPa] Φ[°] C[kPa] Φ[°] Slip-surface Number 5 5 5 5 Min. 19.0 19.5 13.0 17.3 Max. 30.0 24.8 22.0 22.8 Ave. 23.8 22.2 17.3 19.4 SD 4.27 1.96 3.28 1.95 Table 4 The comparison of indoor experiment and in-situ experimental values Type Residual saturated shear Bonding Inner Frictional Angle C[kPa] surpass or exceed than Ave.

So far, the effects of addition of Sc are believed to be positive in most cases, such as to refine grains, improve strength together with ductility and weldability [2].
(a) and (b) respectively, indicating that alloy B shows a great number of coarse particles distributed along the rolling direction and these coarse particles are brighter and whiter than those in alloy A, which means that these particles contain more heavy elements.
Besides, the coarse brittle second phase particles, like the W phase, inhibit the migration of grain boundary and thus has a negative effect on the compatible deformation and plastic flow of the alloy.

Renwick [30] etc. put Wistar rat in nano-TiO2 (29 and 250 nm, respectively) with bronchial injection method 24h, demonstrate that the toxic effect of 29 nm nano-TiO2 is stronger than 250 nm, the toxic effect is related to grain size and superficial area of particle that is accumulated in lung and lead to lung overload and bring out the damage of lung.
Hoyt [31] etc. think that grain size of particle less than 5 μm all can enter into lung that become an important target organ of virulent particles which once is adsorbed by human and other organisms through breath, these nano-particles can hit and deposit the surface of alveoli because the internal Brownian movement, It may damage the natural defense system of human and organisms when the internal consistence exceed a certain amount. 2.3 The effect of TiO2 nanometer materials for liver and kidney.
According to report, 69 percents TiO2 (0.2~0.4 μm) deposit in liver through mainline after 5 and 15 min the number amount to 80 percents [32].
The renal tubular liquid of rat in 80 nm TiO2 group have a large number albumen, the rat in 155 nm group also appear glomerular serious swelling, it explain that nanoscale TiO2 have toxicity for kidney. 2.4 The effect of TiO2 nanometer materials for cardiovascular system.
Nemmar [35] etc. put to use weasand injected method provide Wistar rat with 1 mg/kg and 5 mg/kg virgate nano-TiO2 and dectected that soterocyte were becoming coacervation and depletioninnumbers in blood, moreover presented dose dependent, this is consistent with the Ruckerl’s [36] etc. result that number of platelets decrease accompanied by the increase of soterocyte activation markers CD40 after contacting with some nanoparticle. 2.5 The effect of TiO2 nanometer materials for nerve system.

It is manifested that the laser texturisation is independent to the crystalline orientation of the substrate being irradiated - uniformly texturised surface is obtained on multi-crystalline silicon (mc-Si) substrate and identical absorption enhancement is achieved on different crystal grains.
This makes laser texturisation a very attractive alternative to conventional texturisation method such as chemical etching to be used in mc-Si solar cell production, since the latter is problematic due to the anisotropic etch rates at different crystalline grains [11, 12].
The number of laser shots (Nb) is the scan control parameter defined as the product of spot area and laser repetition rate divided by the product of transverse displacement and laser scan speed.
Despite the difference in quantitative characteristics, increased height with increased quantity of the number of laser shots or laser fluence and decreased density with increased laser fluence, appear as common trends, independent from the ambient pressure.
Similar tendency too holds for increasing the number of laser shots: at any given laser fluence, the accumulation of re-deposits tends to submerge the conical features with increasing Nb.