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In the central part and face of the alloyed layers, the regular grains and intermetallic phases were observed.
The average grain size of the layer was in the range from 100-250um.
The average grain size of the AlMg5 alloy was from 400 to 1000um.
With increased powder amount introduced, an increase in the number of precipitates was observed.
The number of grooves parallel to the sliding direction is evident on all the worn analysed surfaces and ceramic counter-specimens (Fig. 8).

.), the deformation of alloys at elevated temperatures results from long-range atomic-diffusion and/or dislocation movements that can be non-conservative inside the grains.
A more effective way, particularly for casting alloys for applications at relatively high service temperatures and/or under relatively low loads, is to reduce or eliminate grain boundaries as in Ni-based superalloy castings used in the hot-sections of gas-turbine aero-engines.
For agehardenable alloys, second phases function as the major obstacles to dislocations and hence serve as the primary strengthening mechanism among other microstructural features (including point defects, short-range-order, dislocations and grain structure).
Therefore, the second option, i.e. the development of an increase in the number of nucleation sites for the desired omega phase has been examined.
In terms of laboratory detection of atomic clusters or SRO, there are a number of techniques in addition to 3D-AP, but clusters are usually in nanometer size and sometimes SRO is too weak to detect.

This causes a decrease in the number of natural resources available for concrete purposes and damages the environment.
A total number of 78 cylindrical samples were fabricated for the compressive strength test and 39 cylindrical specimens for the splitting tensile strength test, and 26 cylindrical specimens for the HCP test as shown in Table 4.
Batch ID Sea sand FA Sand treatment Number of samples Compressive and split tensile strength HCP FA0PP0 0% 0% washed 9 2 FA0PP10TC 10% 0% unwashed 9 2 FA0PP20TC 20% 0% unwashed 9 2 FA0PP30TC 30% 0% unwashed 9 2 FA0PP40TC 40% 0% unwashed 9 2 FA0PP10 10% 0% washed 9 2 FA0PP20 20% 0% washed 9 2 FA0PP30 30% 0% washed 9 2 FA0PP40 40% 0% washed 9 2 FA20PP20 20% 20% washed 9 2 FA20PP30 20% 30% washed 9 2 FA30PP20 30% 20% washed 9 2 FA30PP30 30% 30% washed 9 2 Testing Methods.
This is because the diameter of the fly ash grains is finer/smaller than the diameter of the cement grains.
So, the small effect of these fly ash grains is to fill the smaller pores in the concrete.

In the process of dispersion, PVP acted as the dispersant and prevented the nickel powders from agglomerating.The Zeta potential of slurry which determined the dispersibility and the reaction condition was tested.The investigation shows that the grain size of Ag-Ni bimetallic powders is similar to the nickel powders, bimetallic powders possesses fine dispersibility and a continuous silver film is formed on the surface of nickel powders by two-times coating.
Recently, the improvement of multilayer ceramic capacitors(MLCCs) has been achieved by the control of the thickness and the lamination number of dielectric layer and led to an increase in the amount of internal electrode, the base metal nickel powders have attracted a great deal of attention as inexpensive internal electrodes in MLCCs due to their good electrical conductivity, high melting temperature and lower cost[4-6].

It initials a particle number for M particle group randomly in N target search feasible solution space.
One is the optimal state that i has been searched so far,which represents particles’ own level, as the individual extreme, grain .
The objective function achieves optimal, part of the nodes voltage exceeding probability: Table 1.The parameters of the system Begin bus End bus Line type Active power Reactive power Begin bus End bus Line type Active power Reactive power 1 2 JKLGYJ-120 142.74 60.6 10 11 JKLGYJ-120 90.63 38.47 1 6 JKLGJ-120 0 0 11 12 JKLGYJ-120 90.63 90.63 6 13 LGJ-50 231.1 98.11 12 15 JKLGYJ-120 285.48 121.2 6 7 JKLGJ-120 0 0 15 4 JKLGYJ-120 0 0 7 5 JKLGYJ-50 285.48 121.2 15 20 JKLGJ-120 0 0 7 8 JKLGJ-120 0 0 20 21 JKLGYJ-95 725.04 307.8 8 3 JKLGYJ-50 181.26 76.95 20 19 JKLGYJ-120 142.74 60.6 8 9 JKLGJ-120 0 0 19 18 JKLGYJ-120 90.63 38.47 9 14 JKLGYJ-50 317.2 134.67 18 17 JKLGYJ-120 142.74 60.6 9 10 JKLGJ-120 0 0 17 16 JKLGYJ-120 142.74 60.6 Table 2 Voltage exceeding probability of part nodes Node number 5 9 17 20 Voltage exceeding probable 0.000000 0.000000 0.000028 0.000086 Table 3 Voltage exceeding probability of part nodes Node number 5 9 17 20 Voltage exceeding probable 0.000000

Results and Discussion Fig. 1 shows the location of indentation with their respective number that has been made on the bonded Au ball bonds for the as-received samples with (a) zero hour of HTS and (b) 1000 hours of HTS.
Fig. 2 shows the graph of Reduced Modulus versus indentation number for each indentation that has been made.
Recrystallization, recovery and grain growth that occur during annealing can affect the microstructures, microtextures and mechanical properties of Au wire [6].
Reduced Modulus versus Indentation Number Graph Fig. 2 shows no particular pattern that can be gathered to describe the changes of Reduced Modulus with indentation location for each area.

After fishing up, the fracture was flat, and there were a number of cracks, air bubbles and corrosion rusts, as shown in Fig. 1.
But after fishing out, the fracture surface and cracks have been seriously corroded, resulting that a large number of information are covered.
Through the micrograph we can see that organization of the casing is mostly made of ferrite, which grain is small, uniform and excluding any inclusion.
(2) There are some large oxide series metallurgical inclusions and a number of micro cracks in the fracture of the Marine oil well casing N80 Q

The joint microstructure of Al-Cu alloy 2519 is shown in Fig.1, the weld microstructure is the α(Al) matrix + eutectic α(Al)-CuAl2, eutectic α(Al)-CuAl2 appears continuous network distribution between grain boundaries and interdendritic of α(Al).
The peak temperature is 476℃, θ' precipitates appear to be long strip and decrease in number.
The peak temperature is 511℃, the number of precipitates increases, the dimension of the most precipitated phases continue to increase and morphology appears to be lenticular, while part of precipitate phases appear to be fine acicular.
Comparison of Fig.4 and Fig.5, with the thermal cycle peak temperature gradually increasing, the number of precipitated phases in thermal simulated specimen decreases, the dimension increase gradually.

The fatigue test was first carried out by using three pieces of specimen for determining the average fatigue life of QT600-3 and the number Nf of circulation is 17422.
The cycling number N was adopted in order of 0.2Nf, 0.3 Nf, 0.4 Nf, 0.5 Nf, 0.6 Nf, 0.7Nf, 0.8 Nf and 0.9 Nf.
The damage variable of specimens at different fatigue cycling number was calculated by the next equation: E E -D ~ 1= (1) Where, D is the fatigue damage variable, E is elastic modulus of nodular cast iron without fatigue damage, E ~ is elastic modulus of nodular cast iron with fatigue damage.
The dislocation in crystal grain can move reversibly and the micro plastic deformation in local matrix occurred.

A recent paper gave an over view of MEAM applications in the study of the bulk properties, grain boundaries, surfaces, and mechanical properties for metals and alloys [7].
The number of atoms in the computational cell is that 4800 Cu atoms with 800 atoms per layer were employed.
The total number of Sn is 500.
The first reason is the manual measurement error, the contact angles manually measured which will introduce the errors; the second reason is triple line moving with time as measure the hidden contact angles, i.e. the hidden contact angles were measure after the triple line moving for cooling to room temperature [10]; the third reason is to define contact line between the liquid phase and solid phase in the process of measuring the hidden contact angles of calculating results; the last reason is difference of time and dimension scale between the calculating model and experimental system: for the dimension scale, the number of the Sn and Cu of the calculating model is far less than the ones of the experimental system, for the time scale, holding time of the experimental process is 600s, while the holding time of the calculating process is about 2*10-11s which is enough for the system equilibrium, i.e. significant differences of equilibrium time between the calculation and experiment were