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The study about micro-morphology of bacteria: The micro-morphology of bacterias showed that they grown on the surface of CMPSW grain densely.
From the Fig. 5, we can see that the number of microbe was large.
Table 1 The elemental composition of samples Element Percentage of element Element Percentage of element Element Percentage of element O 39.1782% Cu 0.2601% Mn 0.2791% Si 21.0284% Zn 0.1191% Na 0.2772% Fe 17.1010% As 0.0856% Ti 0.2674% Ca 10.2750% P 0.0633% Sr 0.0080% S 5.4084% Bi 0.0284% Zr 0.0078% Al 3.1245% Cr 0.0279% W 0.0228% Mg 1.6962% Pb 0.0250% K 0.7168% Fig.1 The concentration of Cu in solution after bioleaching at 1% pulp density Fig.2: The concentration of Cu in solution after bioleaching at 5% pulp density Fig.3 The concentration of Cu in solution after bioleaching at 15% pulp density Fig.4 Cu Leaching rate of CMPSW by different bacterias Fig.5: SEM images of bacterias and CMPSW grain, (a) ×2000, (b)×5000

In some areas, a grain microstructure is found, directional grain growth is clearly visible along the direction of sample production.
SEM image (SE – at left, BSE at right) of Ti-6Al-+TiC material The presented SEM images make it difficult to determine the presence and nature of the reinforcing particles arrangement, which is associated with close atomic numbers of the metal matrix elements and reinforcing elements (primarily titanium).

To date, a number of refractory HEAs were studied and these alloys exhibited many outstanding performances.
As can be noticed, the microstructure of the Al-free VTaTiMo alloys shows the equiaxial dendritic-like grains morphology.
The microstructure of VTaTiMoAlx alloys transforms from equiaxial dendritic-like grains(x=0) into typical dendrite structure(x=1), and the dendrites become thinner and sharper with the increase of Al content as a whole.

The aggregate was foundry sand with a homogeneous grain size, with uniform grains and a mean diameter of 300 μm, with finesses modulus between 3 and 5.
The number presented in the specimen type represents curauá fibers content in weight.

Another method is the formation of a structure with a large number of microcracks which provide multiple changes in the direction of the main crack propagation.
The most prospective methods for increasing fracture toughness of brittle materials are the formation of high destruction energy particles and grains which undergo phase transition accompanied with a volume increase in the ceramic structure.
Development modes of prior free sintering to form a high-density fine grain ceramics after HIP.

A number of existing researches have affirmed the positive role of Si in high speed steel, such as improving the secondary hardness of high speed steel and steel toughness etc. [1-2].
While after quenching at 1200°C, the structure of W6Mo5Cr4V2Si steel is mainly composed by implicit needle or strip-typed martensite, residual austenite and carbide, with average grain size of 40 ~ 60 um.
(3)After quenching at 1200°C around, the quenching structure of W6Mo5Cr4V2Si steel is mainly composed by implicit needle or strip-typed martensite, residual austenite and carbide particles, with average grain size of 40 ~ 60 um around.

The grains are darkened with light gray, gray and dark gray to present the recrystallized, substructured and deformed grains, respectively.
By using three-dimensional calculated electronic charge density, the numbers of electrons that hold in the atomic sphere were evaluated to be 2.30 e for aluminum instead of 3 at the valence band.

Some of the grains of the needle-shaped β-AlFeSi intermetallic are shown to stem directly from layer 1 or 2 such as a peritectic reaciton.
Moreover, the layer 2 is composed of small irregular dispersed grains, which seems to be deteched from the layer 1.
For semi-quantitative analyses of each phase composing the intermetallic layers and the microstructure, the composition of them (indicated by the number in Fig. 3) was analyzed by EDS and summarized in Table 2.

It was found that preliminary mechanical activation (MA) of powder mixtures resulted in a substantial decrease in the ignition and combustion temperatures during SHS that allowed controlling the grain size of the products [3].
The broadening of copper and titanium lines is caused by grain refinement and accumulation of microstrain during the plastic deformation.
The completeness of the reaction in the MA-ed mixture can be attributed to the drastic increase in Ti/B interfaces during MA-processing, which provide a large number of new ignition sites in the sample.

The off-axis reduces also the number of wafers that can be sliced from a boule of given length.
However, a more growth related origin was found in the region between interacting grains, typically at boundary cusps.
This may be explained in the following way: under low supersaturation the atoms can be preferentially arranged at the grain boundary, however, at higher supersaturation there is less time for diffusion and atomic disorder is expected, with defect formation as a result.