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To increase the electrical conductivity, it is necessary to increase the number of oxygen vacancies in the crystal and obtain a non-stoichiometric titanium dioxide, TiO2-x [3,4].
Structural features (phase composition, micro strains, deviations from stoichiometry, grains size) have characteristic effects on ceramics properties.
Fourier transform infrared (FTIR) spectra were measured on Scimitar Series model Varian 800 FTIR spectrometer in the wave number region 400-4000 cm-1 with spectral resolution 4 cm-1.
The most intensive growth of ceramic grains was observed in temperature range 1100 to 1250 °C. [2].

The propagation of Lüders bands is influenced by many factors including crystal structure, grain size, composition and microstructure, shape and stiffness of the testing sample, strain rate and the type of loading.
Fig. 2 Sample No. 27 a) uniaxial tensile test, b) biaxial tensile test Fig. 3 Detail of plastic undeformed parts of sample after uniaxial tension test Table 2 Mechanical properties of material identified by uniaxial tensile test Sample number Additional information Thickness [mm] Rp0.2 [MPa] Rm [MPa] A50 [%] 27 (0°)1 TH 415 CA 0.18 464.2 457.7 20.38 27 (0°)2 TH 415 CA 0.18 465.2 451.7 22.25 27 (0°)3 TH 415 CA 0.18 422.6 419.4 22.21 ÷27 0° TH 415 CA 0.18 450.67 442.93 21.61 27 (90°)1 TH 415 CA 0.18 491.9 489.2 3.28 27 (90°)2 TH 415 CA 0.18 518.0 511.4 0.10 27 (90°)3 TH 415 CA 0.18 501.9 498.9 2.27 ÷27 90° TH 415 CA 0.18 503.93 499.83 1.89 For the purpose of detection the mechanical properties of tested plates was making a biaxial tensile test.
Table 3 Mechanical properties tested steel sheets identified by biaxial tensile test Sample number Additional information Thickness [mm] Rp0,2 [MPa] Rm [MPa] A [%] hdome [mm] 27 1 TH 415 CA 0.18 367.7 509 12.72 17.8 27 2 TH 415 CA 0.18 374.8 508.5 13.28 18.2 27 3 TH 415 CA 0.18 366.7 503.9 11.77 17.1 ÷27 TH 415 CA 0.18 369.73 507.13 12.59 17.7 Experimental methods Uniaxial tensile test was carried out on the device TIRA test 2300.
After uniaxial tensile test in the direction 0° microstructure showed significantly elongated grains in rolling direction which is the result of the double reduction (Fig. 6a).

., random distributions of grain size, slip system and grain boundary, and marco defects such as porosity, crack, and casting defects.
Vickers Hardness Initiation cycle Specimen life m C 1 2 3 30 (1) where refers to the series number, refers to the specimen number, represents the original factor series, represents the new factor series after the process of grey relation generation, and indicates the nominal value specified for new series.

This experiment is focused to analyze the influence of machining technology on the quality of the machined surface and surface quality of the notch using a number of parameters in relation to the loading capacity [4].
Both wheel made by corundum are characterized by grains with higher geometric regularity [6,7].
The grain has a higher removal ability, thanks to self-sharpening effects.
Figure 4 shows number of maximum cycles reach during loading test.

San et al. [3] reported from their study in microcutting of soda-lime glass performed by endmilling process (side-milling performed by using up-milling technique) having 4-flute, TiAlN coated, super fine grain cemented carbide end mill (dia. 3mm) at 1000 rpm that at very small radial depth of cut (2 μm), ductile cutting can be achieved at higher feed per edge which is cardinal to prevent plowing and subsequent surface deterioration due to minimum chip thickness effect.
A micro-grain cemented carbide tool with plasma CVD coating (diameter = 2 mm, number of flutes = 2) was used for machining rectangular pieces of soda lime glass (dimensions = 20 mm x 15 mm x 5 mm, Composition: 73% SiO2, 14% Na2O, 9% CaO, 4% MgO, and 0.15% Al2O3).
Table 4: Possible optimal solution for end milling Number spindle speed feed critical depth Desirability 1 39.70 7.20 497.179 1 Selected 2 37.07 7.19 502.631 1 The critical depth contour plot for solution 1 is shown in Fig. 3(a).

When the abrasive grains uniformly and progressively to the flow path surface or edge working, can produce deburring, polishing, chamfering role [4, 5]. 1 Establish common rail mathematical model of the solid-liquid two-phase flow Study described by Newton's laws of motion of the particles, two-phase coexist on the same point in space, their compliance with their own momentum, mass and energy transfer equation, the two phases interphase forces and shared by pressure field coupled to each other [6].
Standard model turbulent kinetic energy dissipation rate and the transport equation are: (1) (2) Where, is time, ; tensor represents the subscript, represents the coordinates of the tensor, represents a velocity vector in Component 3 coordinate axis; said turbulent kinetic energy, ; said the average velocity gradient caused by the generation of turbulent kinetic energy item, ; represents the turbulent kinetic energy K corresponding Prandtl number; said dissipation rate corresponding Prandtl number; , representation model empirical coefficients; in the formula (1), (2), and calculated as follows: (3) Among them, said turbulent viscosity, ; represents a model coefficient; represents an intermediate variable; represents an intermediate variable; E represents when the average strain rate tensor modulus; represents an intermediate variable; represents when both rotation
With the increasing inlet velocity, dynamic pressure inside the common rail is increasing, abrasive grains and stream channel wall effect is more intense, more conducive to the abrasive flow ultra-precision machining. 3.3 Speed Numerical Analysis In order to better analyze the processing characteristics of the abrasive flow, to abrasive flow machining abrasive flow characteristics were numerically analyzed, the velocity vector image shown in Figure 7.

Based on the above analysis and experiments conducted in this paper, the basic composition of the researched material is determined in such a proportion (atomic number) as: 48%Ti, 48%Al, and 2%Nb.
Table1 Heat treatment schedule of samples Sample number Heat treatment temperature(℃) Heat treatment time(min) B4 630 120 B5 1150 120 B6 1200 60 B7 1250 60 This experiment has set up four temperature points for heat treatment test at 630℃, 1150℃, 1200℃, and 1250℃ respectively, and the heat treatment results of samples refer to the Table 1.
The double-phase TiAl alloy grain formed is of flake shape, with thickness of about 1um and length of about 6~ 10um and the grains are obviously bigger compared with the ones before thermal treatment.

Using such a model allows engineers to reduce the number of tests required to determine the optimum parameters for ultra-rapid cooling and to design the casting mold accordingly, and as a result, to reduce the total cost of obtaining a bulk amorphous metallic alloy.
Bulk amorphous alloy The advantages of amorphous metallic alloys are obvious and determined by the fact that there are no grains and no grain boundaries, no dislocations and no other structural discontinuities.
The finite element analysis model provides a tool that allows to evaluate the capability of obtaining amorphous structures for parts with known geometries, even during the design stage (before making any experiments) or to reduce the number of experiments necessary to evaluate which is the largest amorphous part that can be obtained from a given alloy.

Ta is a multivalent element with effective ionic radius (6-fold coordination number) of 0.86 Å, 0.82 Å and 0.78 Å for Ta+3, Ta+4 and Ta+5, respectively.
AC susceptibility from 30 K to 120 K was performed by an AC suseptometer from Cryo Industry model number REF-1808-ACS to determine susceptibility transition temperature and intergranular critical current density.
This sample showed granular-liked grains structure and closed packed microstructure with defined grained boundaries.

(a) 2000 4000 6000 8000 image quality 0.2 0.1 0.0 number fraction prior austenitic grain boundary prior packet boundary wide lath-martensite M–A phase (b) prior block boundary 111 001 101 A D C B Fig. 3.
A small number of voids first originated primarily at the interface between the large M–A phase and the matrix with a wide lath-martensite structure, where there was a highly localized stress concentration.
(1) Softened wide lath-martensite structure matrix (2) Plastic relaxation of localized stress concentration by strain-induced transformation of metastable retained austenite Suppression of void formation and stable crack extension prior austenitic grain boundary (am*+gR) fatigue crack stretched zone (I) fine dimple (II) coarse dimple (II) packet boundary am* am q M-A block boundary void gR (I) Fig. 5.