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This statistics has been carried out from data of twelve biggest producers of coke silica.
Material corrosion gradually occurs displaying as a modification in pore distribution on behalf of greater pores and reduction of mechanical strength of walling.
Fig. 1 Silica stones for a coke oven battery Fig. 2 Silica, enlarged 40-times, optical microscope Fig. 3 Silica, enlarged 2100-times, REM Trends in field of the coke industry silica The development of coke silica quality marks aims to increase the density, and thus the thermal conductivity of silica and the generated reduction of the coke coking times.
Using silica of these parameters increases the heat transfer through the combustion chambers walls, which induces the coking time reduction.

Different types of sensors and actuators are fitted in respective places in order to collect the data and send it to the processor.
In injection mode the reduction in HC is 30% at 3655 rpm over carburettor mode.
As engine speed increases, less residual exhaust gases are present in injection mode, hence reduction in HC emissions.
It is observed that at 2500 rpm the reduction in CO in injection mode is 20 % lesser than that in carburetor mode.

Composition (w%) Vickers hardness (HV) 80%Cu-8%Ni-4%Ag-8%CeO2 69.54 80%Cu-4%Ni-8%Ag-8%CeO2 97.10 80%Cu-8%Ni-4%Ag-8%La2O3 70.82 80%Cu-4%Ni-8%Ag-8%La2O3 62.30 X rays powder diffraction data were collected with a conventional diffractometer Rigaku MiniFlex II, using λCuKα radiation and fixed monochromator.
Phase Weight fraction (%) Cu 92.8 Ag 5.2 CeO2 0.3 CuO 0.5 NiO 0.9 CeCu2 0.3 Table 4: Fractional atomic coordinates of refined phases for sample with the composition 80%Cu-8%Ni-4%Ag-8%CeO2 Phase atom x y z Cu Cu 0.020833 0.000000 0.000000 Ag Ag 0.020833 0.000000 0.000000 CeO2 Ce 0.020833 0.000000 0.000000 O 0.041667 0.250000 0.250000 CuO Cu 0.020833 0.000000 0.000000 O 0.041667 0.250000 0.250000 NiO Ni 0.083333 0.000000 0.000000 O 0.250000 0.500000 0.500000 CeCu2 Ce 1.000000 0.258500 0.250000 Cu 1 1.000000 0.435000 0.006400 Cu 2 1.000000 0.147600 0.250000 Cu 3 1.000000 -0.181300 0.250000 Cu 4 1.000000 -0.439700 0.250000 Cu 5 1.000000 -0.100000 0.250000 The fact that the mass fractions of phases CuO e NiO are higher than the ceramic oxide CeO2 indicates that the oxidation of metals occurred more from the reduction of cerium that stemmed from atmospheric oxygen.
That is because cerium has a higher reduction potential than copper and nickel, which caused the formation of metallic cerium and its subsequent diffusion in the metallic matrix during the thermal treatment.
The results indicate the presence of Cerium contributes to the oxidation of the metallic matrix due to its high reduction potential.

In addition, the base demand following at table 1: Table 01: Base node Demand [l/s] Nodes 1 2 3 4 5 6 7 8 9 10 11 12 13 Demand -210 0 0 0 70 0 7 0 70 20 0 0 0 Table 03: Pump curve Data pipe length [m] and diameter[mm]: 2-300-250, 3-200-200, 4-150-200, 5-200-200, 6-200-250, 7-200-200, 8-200-200, 9-1000-100, 10-125-200, 11-125-200, 12-125-200, 13-150-200 and 14-200-200.
It was evident that the use of routines optimizers coupled to hydraulic simulators are powerful tools in the operation of water supply systems, leading to significant reductions in energy consumption.
It can also be observed from the results presented that the reservoirs of varied level downstream of the pumping play a crucial role in the reduction of energy consumption, whereas during peak values ​​are emptied until the next minimum, thereby reducing the consumption by the pump.
Finally, the new paradigms imposed by the deep need for reduction of energy consumption has led the sanitation industry to rethink their operating routines.

The used material data were published in [1].
Fig. 4 Reduction of stress intensity factors due to residual stresses in dependence on the crack length for different particle shapes (VFF = 25%, c/b = 0.4).
Fig. 4 shows reduction of stress intensity factors due to acting residual stresses in both studied states (with and without consideration of residual stresses) and mutual comparison of influence of residual stresses in composite with spherical and elliptical shape of particles.
The results can be summarized to following points: i) the presence of residual stresses significantly reduces values of stress intensity factors (up to 30% in studied case), i.e. significantly influence the crack behavior in particulate composite and the crack propagation rate, ii) shielding effect of residual stresses contributes to the crack deflection close to the particle – crack propagates only in the matrix without direct interaction with particles, iii) the shape of the particles influences the reduction effect of residual stresses.

Thus, the mass of hollow fan blades which are made by pressure welding combined with superplastic forming is considerably lower than that of solid ones that results in more efficient metal use and finished product weight reduction [3].
Experimental data for uniaxial compression of the two materials considered at the welding temperature were used to formulate the constitutive relations for the DEFORM-2D system.
In this particular case, the combination of these relief surfaces is equivalent to creating considerable amount of friction, i.e. alloy movement along the joint surface decreases which leads to a significant reduction of the shear strain component near touching surfaces, and, as a consequence, results in worse quality of a weld as compared to welding samples with flat surfaces (sample I).
Thus, the relief made contributes to the deformation localization in the solid-state weld zone and, as a consequence, to the reduction of the pore relative length which improves the quality of joint.

Finally, calcination and reduction processes were carried out to obtain MWNT/Cu composites.
Fig. 1(a) shows powders of pure copper acetate, and Fig.1(b) shows the mixture of copper acetate and MWNT after the calcination and reduction processes.
(a) (b) Figure 1 (a) SEM image of copper acetate powders (b) SEM image of the mixture of MWNT and copper acetate after the calcination and reduction processes.
However, the decrease in the mean values was within ranges of standard deviations of measured electrical resistance data.

From these data it can be observed that increasing the Cl/Si ratio from 0.05 to 0.5 the leakage current increases slightly from 2.05×10 -6 A to an average value of 3.08×10 -6 A.
The further increase of the Cl/Si ratio to 2.0 shows a reduction of the EH6/7 level, whose concentration becomes 7×10 12 cm-3 and the absence of the Z1/Z2 and RD1,2 levels.
The correlation between I-V and DLTS measurements shows that the reduction of the leakage current is related to the reduction of the generation current due to the level EH6/7.

Varying the withdrawal rate changes the primary and secondary dendrite arm spacing, and affects chemical segregation [3,4], and any reduction in chemical segregation would result in a significant reduction in heat treatment requirements.
It has also been proved that higher withdrawal rates result in a reduction in the number of solidification porosity [5].
Fig.1 The as-cast microstructures of the experimental alloy at various withdrawal rate: (a, b) 2mm/min; (c, d) 7mm/min Table 1 Statistical data from metallographic measurements of DAS and porosity Withdrawal rate [mm/min] PDAS [µm] SDAS [µm] porosity amount diameter [µm] volume [%] 2 356 126 574 13.7 0.24 4 335 97 613 12.9 0.17 6 307 64 498 12.9 0.11 7 283 57 804 10.8 0.2 10 269 51 1618 10.6 0.33 The compositions of the dendritic and interdendritic regions were determined by electron microprobe to investigate the difference in the extent of microsegregation resulted from varying withdrawal rate.

For example, the spectrum curves for the mean lifetime of positron changes as a function of the sample deformation or annealed temperature; [2-6] advantages of these methods in obtaining both qualitative and quantitative data on behavior are pointed out.
Samples of 7075 alloy were deformed to 25 % thickness reduction, and consecutively subject to isothermal annealing.
Figure (5 ) shows the resistivity as a function of annealing temperature for 7075 alloy plastically deformed to 25% of thickness reduction at room temperature.
Figure 6(a) Variation of resistivity as Figure 6(b) Variation of resistivity as a function of annealing time at 643 K a function of annealing time at 663 K Figures 6(a, b, c, and d) show the isothermal annealing curves measured at 583, 603, 623 and 643 K respectively of the samples deformed to 25% thickness reduction.