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Every cell in the grid system will be assigned a random number (0-1) and the cell whose random number less than will be selected as a core.
(vi) A new random number will be assigned to neighboring cells of each growing pores.
The neighboring cell in direction will become part of macro pore if its random number no greater than.
Considering the computational time and numerical stability, the grid number of the 2D computational domain is set to be.
(3) where is the local non-dimensional relaxation time, which is equal to in solid (grains) phase and in the gas (pore) phase respectively.

Additionally, optimization of the number of nodes to minimize the CPU memory consumption is necessary, owing to the large number required in laser heating simulation.
Dimensions of the sample were 0.75×0.45×0.35 mm3 which is large enough for the temperature to achieve the steady estate, at the values of scan speed applied, and, conversely, lower than the characteristic size of the mineral grains (in the order of 0.5 mm to 2 mm) Time steps used were different during the heating, Dt = 5 ns, and the cooling (Dt depending on the repetition frequency f), owing to the characteristics of the pulsed laser treatment.
FEM simulation features FEM Simulation Features Sample dimensions 0.75×0.45×0.35 [mm3] Mesh sizes 30, 15, 5 and 1[µm] Elements distribution (XYZ): 130×70×15 Total number of elements: 136500 Total number of nodes: 148816 Number of pulses 50 Time step (heating): 25 ns Time step (cooling): Depending on f In order to obtain a first estimative of the heat diffusion towards the bulk, the temperature at the center of the laser spot was obtained.
In the case of a number of pulses, however, a time is required for every point of the sample to achieve the steady state, owing that the temperature in the centre of the spot, and of the sample, has not returned to the initial value before irradiation with subsequent pulse.
Evolution of the maximum temperature reached after a number of pulses a), and temperature variation as a function of time in the centre of the surface, b).

Table 3.1, The original sections representative deflection value and resilience modulus Pile number Representative deflection (0.01mm) The old road top modulus (MPa) Top surface soil modulus (MPa) 20 cm bottom modulus (MPa) K0+000~k1+000 156.45 98.53 23 48.18 K1+000~k2+000 135.63 120.92 32 61.64 K2+000~k3+000 105.01 156.19 53 87.40 K3+000~K4+000 148.50 110.44 27 54.81 K4+000~K5+000 157.74 103.97 25 51.32 K5+000~K6+000 153.25 94.67 20 44.89 Cool regeneration of the cement stabilized of base course design results The pavement adopt cement stabilized cool regeneration technology.
Construction method used in the process of sand filling real-time detection of compaction, some random shown in table 3.5 situation, accord with compaction degree requirements Table 3.5 Part of random compaction degree Sampling pile number Water content (﹪) Dry density Compaction degree Sampling pile number Water content Dry density Compaction degree K1+220 4.1 2.306 99 K3+920 3.8 2.282 98 K1+560 3.9 2.168 93 K4+680 3.5 2.296 98 K2+150 3.6 2.304 99 K5+260 3.6 2.224 95 K2+900 3.5 2.283 98 K5+570 3.9 2.187 94 K3+305 3.4 2.213 95 K5+960 5.0 2.181 93 The unconfined compressive strength sampling conditions of base course： The construction process of cold regeneration of the base course seven days to cement the unconfined compressive strength with according to the highway engineering inorganic material test procedures in feeding stable T0805-94 methods of random situation. table 3.6 shown.
Table 3.6 7 days the unconfined compressive strength of sampling Construction pile number Number of parts coefficient Cv (%) Average compressive strength(MPa) Represent value Rc-1.282S K0+000~K1+160 6 6.0 3.19 2.95 K3+160~K4+005 6 15.3 3.43 2.76 K4+560~K5+580 9 11.7 3.34 2.84 During the construction of got cold regeneration of cement on-site ,sampling test ,got eight points altogether ,core samples close-grained and hole wall smooth ,core sample length comply with the design requirements.
After all sections regimen use 5.4m Beckman beam deflection situation instrument measuring pavement deflection shown in the table 3.7 Table 3.7 Deflection testing situation Sections pile number Point number average (0.01mm) Three-parameter stress-life (0.01mm) Representative deflection (0.01mm) K0+000~k1+000 100 24.07 18.39 51.66 K1+000~k2+000 100 30.48 10.71 46.55 K2+000~k3+000 100 25.68 12.41 44.29 K3+000~k4+000 100 27.69 11.58 45.06 K4+000~k5+000 100 25.72 9.96 40.66 K5+000~k6+000 100 27.84 9.28 41.76 Conclusion (1)Make full use of the original rood miller disused material plane ,and avoid waste material covering ,having use to protect the ecological environment ,At the same time saving a lot of building materials ,both saved the resources ,and reduce the investment and reduce the cost (2)The old road that add a store the base course is highway maintenance traditional treatment ,this leads to continuously improve road elevation make more and more narrow road width ,and lap with

The mutual collision between balls and alloy powders, the cold weld between alloy powders, and the mutual diffusive between atoms occurred during high-energy milling process, thereby increasing crystal defects and grain boundaries [11,12].
The MgNi and MgNi+5%B alloy powders consist of irregular particles, with a grain size less than 5μm in diameter, and the MgNi+5%B alloy powders had slightly more uniform diameter than that of MgNi alloy powders.
%B alloys as a function of cycle number Table 4.
The maximum discharge capacity Cmax and cycle capacity retention rate Sn of the MgNi+x%B alloys Samples(x) Cmax(mAh/g) S20(%) HRD400(%) HRD800(%) Io(mA/g) MgNi 320.5 17.9 43.2 27.9 60.5 MgNi+2%B 337.1 17.8 53.4 30.5 158.3 MgNi+5%B 358.6 24.5 58.3 32.2 293.5 MgNi+10%B 347.7 29.4 48.6 28.5 112.6 Fig. 6 shows the discharge capacity of the MgNi+x%B(x=0,2,5,10) alloys with cycle numbers.

It is known that the amount of stored elastic energy in deformed polycrystals is dependent upon the grain orientation, and subsequently the release of this energy and evolution of the microstructure and texture during annealing is very much dependent on the starting texture and microstructure [1].
The models are highly dependent on assumptions made about the initial dislocation network and contributions from both the dispersed dislocations and those in the growing cell wall/sub-grain structure.
A tensile increase can result from dislocations being pulled into the denser regions (walls) clearing the interior region for a lattice expansion, while the subsequent increase in the compressive component may be due to the thinning of the cell and increasing the number of dislocations within the interior cell.
After recrystallization (>300°C) there is a distinct increase in the lattice strain due to both the annihilation of a large number of dislocations and the likely dissolution of Mg and other particles into solid solution causing the lattice to dilate.

Two phases of Stainless Steel Two phases of stainless steel is stainless steel which has a mixture of structures from ferrite bcc and austenite fcc besides that designed a number of content austenite phase is the same.
Its growth begins at the ferrite grain boundaries and then grows into the ferrite grain according to the crystallographic directions.
Method of TIG welding using shielding gas mixed with nitrogen can produce a relatively equal number of phases between ferrite - austenite at welding with 95 % argon + 5 % nitrogen in the welding speed 3 and 4 mm/sec.

Cavitation has also found application in a number of commercial products to clean or breakdown materials because of producing extremely high energy densities [3].
Such a device has also been used by a number of other scientists [10, 11].
Laser beam processing and subsequent rapid cooling of materials subjected on the cavitation erosion leads as a rule to grains refining and, due to diffusion retarding, creates the state of residual stresses within the processed material.
Refining of the grains and a decrease in micro cracks length causes the material to erode away in smaller pieces and at a lower rate.

This complex phenomenon possesses a great number of challenges for theoretical analysis.
In the equiaxed zone the crystal grains are freely moving in the melt.
At the macroscopic scale, liquid flow in the columnar mushy zone can be modelled by treating this region as a porous medium [1], while in the equiaxed mushy zone some models of grain suspension are applied.
However, a rather limited number of attempts were undertaken to measure this property and to associate it to the current morphology of the columnar mushy zone, i.e. to spacings of the primary and the secondary dendrite arms.

On the other hand, when the quenched specimen underwent subsequently the temper treatment shown in Table 2, sulfide would be formed or S would segregate in the grain boundary, because the solubility limit of S was estimated to be null at 873K [11,12].
But a small number of a Cr sulfide phase was also observed as submicron particles in the S-doped steel tempered at 873K for 18ks.
∑=i xMw ii ox , (2) where Mi (kg/mol) is the molecular mass of each oxide and xi (mol) is the number of each oxide moles, and both Mi and xi were estimated by using the experimental data obtained from EDS analysis and the cross-section observations.
It was also found that the steam oxidation resistance was improved when S made a sulfide or segregated in the grain boundaries, but never improved when S existed in a solid solution.

Varying quantities of material ranging from small to large can be processed, and the resulting powders usually display nanometer-sized grains.
McKamey of Oak Ridge National Lab., was mixed with 5 wt% and 10 wt% Si (<45µm grain size, 99.5% purity), giving the atomic compositions Fe64Al26Cr1Si8, and Fe59Al24Cr1Si16, respectively.
v (mm/s) 0 10 20 30 p(Bhf) Bhf (T) Journal of Metastable and Nanocrystalline Materials eVolume 12 33 A high number of iron atoms in antisite position (replacing aluminium atoms) and vacancies (mostly of iron) are present in the material.
After thermal annealing the Mössbauer spectrum of the Fe64Al26Cr1Si8 sample displays a sharper magnetic distribution shifted to higher values of hyperfine magnetic field, indicating a reduction in the number of configurations for the Fe atoms in the bcc structure.