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However, because of the applications of porous media, it will be jammed by the mineral grains easily. (2)Gravel layer microbubble generator: The gravels will be placed in the grid cell lattice, the diameter of which is 80-200mm, and then there will be 500-600mm thickness gravel layer.
This structure reduce the clogging of mineral grains, but the air consumption is much more than others, and the size of the bubbles generated is not regular, which will have some bad effects on the mineral separation. (3)Electrolytic microbubble generator: The microbubbles, which are generated by this type generator, will be very homogeneous in density, and the diameter of the microbubbles is 0.02-0.06mm.
In the flotation process, the interaction between the bubbles and the particles are as follow: (1) Collision: according to the Stocks’ number, collision can be divided into viscous collision and inertial collision.

The X-ray diffraction peak intensity of PST powders increase with annealing temperature increasing and the full width at half maximum (FWHM) decrease indicating crystallinity enhanced and an increase in grain size with increasing annealing temperature up to 650℃.
The wall of the PST nanotube is very thin and there are some particles on the surface, which illustrates that PST nanotube is polycrystalline structure comprised by numbers of nano-grains.

By research and operational experience, it has been established that the microstructure of high-speed R6M5K5 steel produced by the traditional method (fig. 2a) is characterized by nonuniform grain size and nonuniform distribution of the carbide phase (light spots).
Microstructure of forged high-speed steel (a) and powder steel (b) By contrast, when pressed parts are produced from metallic powders that have been generated by spraying, their microstrukture is characterized by small grain size and excellent uniformity, and pressed steel tools are very strong and ductile.
The number of displacement cycles depended on cutting modes, quality parameters and geometrics of the cutter, machine stiffness, and other factors.

Acknowledgements The financial support from the National Key Project of Science and Technology (Grant number: 2012ZX06004-012) is gratefully acknowledged.
Suzuoka, Lattice diffusion and grain boundary diffusion of cobalt·in Iron, Trans.
Herzig, Lattice and grain boundary diffusion of niobium in iron, Z.

According to the ratio of stoichiometric number, the required glycine and inorganic salts can be determined.
According to Scherrer equation L=0.94λ/(βcosθ) [12,13], where L is grain diameter, λ is the wavelength of the incident X-ray, β is the diffraction peak full width at half maximum (unit: radian), and θ is the diffraction peak corresponding to the incident angle.
What can be seen very clearly from Figure 2(B) are the inerratic continuous lattice lines of Nd1.9Al0.1Zr2O7 nanocrystals, indicating the sample has full crystallization, and the grain boundary can be seen clearly.

Temperature [°C] 800 900 Milling time [h] 3 6 9 3 6 9 Specimen number Hardness [HV] Hardness [HV] 1 F1 46.4 40.49 39.61 38.6 46.47 34.65 F2 62.5 36.49 34.65 47.9 44.87 33.17 2 F1 57.4 44.66 36.88 46.8 45.55 44.90 F2 63.0 38.82 31.07 45.7 43.48 38.75 3 F1 54.0 40.98 34.05 45.1 40.49 36.17 F2 47.9 39.07 31.40 49.8 49.97 36.94 4 F1 51.0 38.52 34.81 51.7 42.87 38.41 F2 49.1 37.31 34.87 47.3 51.46 36.94 5 F1 58.6 56.50 32.02 50.9 50.16 38.37 F2 44.2 46.37 31.30 46.5 49.50 38.50 Average 53.41 41.92 34.07 47.03 46.48 37.68 Two measurements were obtained from each specimen, one corresponds to the side parallel to the direction of application of compression (Face 1: F1), and other is from the face parallel to the direction of application of compression (Face 2: F2).
In the specimens with 9 h of milling and sintered at 800 ° C there is the presence of irregular grains which causes the decrease in hardness.
Hug, “Influence of spark plasma sintering conditions on the sintering and functional properties of an ultra-fine grained 316L stainless steel obtained from ball-milled powder,” Mater.

From the FESEM images, it is evident that the MWCNTs evenly distribute on the alumina grains, and the length of MWCNTs is not more than 2 micrometers, which results from acid pickling and ultrasonic treatment for the MWCNTs.
There are a large number of pores in the composites, and the addition of MWCNTs will inevitably result in an increase in porosity and also inhibit the alumina grains growth during sintering.

Up to now, a great number of studies with the effect of inclusions on internal cracks have been done [6-8].
In addition, the original grain of austenite is coarse, and carbon is dilution, the distribution of the austenite grain was banded along the main deformation direction as a result of the limited recovery after pressure processing.
As a conclusion, the difference of expansion quantity in segregation zone due to the presence of banded structure formed during heating or cooling and the bulky inclusions formed in macro-segregation zone can result in the larger stress concentration during forging, and the ingot will be cracked initiation along the grain boundary, which propagation is quite easy under upsetting forging stress.

The intensities of Ti, Al and C powders diffraction peaks decreasing significantly with the milling time, while their width increasing at the same time, which is mainly due to grain refinement and buildup of defects and formation of internal strains in the process of milling.
As shown Fig. 3 (a), a large number of light grey phases are distributed uniformly along the boundaries of the matrix.
The Ti3AlC2 formed around the boundaries of TiAl3 can refine grains and hinder the slip of dislocation, and thus strengthening the composite.
Superposition of grain size and dispersion strengthening in ODS L12–(Al,Cr)3Ti [J].

The two distinct regions are seamlessly coupled by energy calculation, and can adjust each other according to the movements of crystal defects, e.g. dislocation, grain boundary.
After picking out Nrep representative atoms, the displacement field of the entire system can be approximately expressed as: , (3) The total energy can be calculated as: , (4a) , (4b) where Nloc and Nnl are the numbers of representative atoms in the continuum and atomistic regions.
Dupont, Grain growth behavior at absolute zero during nanocrystalline metal indentation, Appl.
Wang, Investigation of grain boundary activity in nanocrystalline Al under an indenter by using a multiscale method, Chin.