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With the recent development of nano-processing technology, research has been actively conducted to manufacture au uncooled type infrared sensing device having a number of Focal Plane Arrays (FPAs), and the developed nano-processing technology allows manufacturing of a heating type infrared sensing device that operates at room temperature and has high sensitivity.
In this experiments, we have found invresing TCR with increasing annealing temperatures that may be related to variations in the grain size. 25 30 35 40 45 50 10 20 30 40 50 60 70 80 -0.85%/ o C -0.906%/o C -2.75%/ o C Resistance (k?
This change could be attributed to the grain orientation and the internal residual stress between grains and between the films and the underlying substrate. 20 30 40 50 60 70 80 40 50 60 70 80 90 100 Temperature [ oC] Dielectric Constant V 1.9W 0.1O 5 (300oC) Fig.4 Dielectric constant of the V1.9W0.1O5 thin films on Pt/Ti/SiO2/Si substrates annealed at 300°C, as a function of temperatures.

The grain size and roughness of deposited layers obtained with the PPMF were reduced [12].
Ispas et. al. [17] reported that the number of grains deposited in PPMF was much higher comparison to the absence of magnetic flux.
The influence of the PPMF on the grain size and strain of Ni electrodeposited layers can be calculated from XRD data by using the Debye-Scherrer [12].

By introducing a relatively small number of rare-earth ions, the lattice expands resulting from larger ion radius of Eu3+ than Fe3+.
However, redundant Eu3+ ions aggregates on the grain boundaries forming EuFeO3 shown in Fig. 1(c), which leads to compressive pressure exerted on the ferrite lattice according to relative papers [8, 9].
Table 1 Magnetic properties of Mn-Zn ferrite annealed at 700oC Substitution [x] Ms [emu/g] Mr [emu/g] Hc [Oe] 0.00 68.4 8.8 81 0.01 63.4 9.5 89 0.02 71.7 12.7 81 0.03 68.1 11.6 80 0.04 69.1 12.6 86 (a) x = 0.00 (b) x = 0.02 (c) x = 0.03 (d) x = 0.04 Fig.3 SEM micrographs of Eu3+-substituted Mn0.65Zn0.35Fe2-xEuxO4 ferrites annealing at 700oC Fig. 4 Magnetic hysteresis loops of ferrites: (a) Mn0.65Zn0.35Fe2O4 powders annealed at different temperature; (b) ferrite powders with x = 0.00-0.04 annealing at 600oC The SEM images (shown in Fig. 3) of substitution on Mn-Zn ferrite with x= 0.00, 0.02, 0.03 and 0.04 annealing at 700oC indicate that the grains in morphology spherical shape with Eu3+ ions dopants are somewhat expanded in dimension, but all the particles display low crystallinity.
That behavior could be explained as follows: On one hand, the magnetization increases with direct relationship to grain size of crystal and purity of the ferrite attributed to rare-earth ions substitution [10,11], corresponding with Fig. 1(c) and Fig. 3.

It appears that etching first occurs at the centre of grain structures with the grain boundaries remain un-etched as grain boundaries are mostly defined by threading dislocation [15].
In consequence, higher number of electron to take part in the excitation and recombination process in porous samples compares to the lesser surface area of as grown sample.

After the experiment, in the tube samples were controlled: residual stress, metal grain size, hardness and resistance to intercrystalline corrosion (ICC).
Table 1 The results of measurements of properties of the tubes 20 × 1,5 mm made of steel 08Cr18Ni10Ti after laboratory experiment № t, oC τ, sec Cooling type* q0, MPa q1, MPa I1, A Grain size балл Intercrystalline corrosion, mm HRF σφφ ,MPa 1 950 60 EXT-A - - 0 9,8 0,035 74,0 -16.2 2 1100 37 EXT-A - - 0 10 resistant 75,0 -13.5 3 1000 30 EXT-A - - 0 10,9 0,025 72,0 -17.9 4 1050 35 EXT-A 34,3 25,0 0 10,9 resistant 75,0 -82.5 5 950 30 EXT-A 34,3 28,0 0 9,8 resistant 74,0 -54.2 6 1000 30 EXT-A 34,3 25,5 0 10,9 resistant 75,0 -63.4 7 1050 34 EXT-A 34,3 24,5 0 10 resistant 72,0 -96.2 8 1000 28 EXT-W - - 0 9,8 0,035 73,5 -12.0 9 1000 35 EXT-W 34,3 25,5 0 9(8) resistant 71,5 0,0 10 1000 56 INT-W - - 0 9,10,8 resistant 70,5 26.2 11 1000 40 INT-W 25,8 18,4 0 8,7,6 0,06 76,0 98.0 12 1000 35 INT-W - - 45 10 resistant 76,5 82.2 13 1000 30 INT-W - - 45 10 0,035 72,5 56.4 14 1030 40 EXT-W 16,6 9,8 40 10,9 resistant 73,5 -103.1 15 1000 35 EXT-W 16,6 9,8 40 9,10,8 resistant 70,0 -110.4 16 1050 45 INT-W
The regime that allows you to get the tangential compressive residual stresses in the pipe wall, providing grain size of at least 8, and resistance to ICC, and which can be recommended for industrial use, as follows: - current density - 12 ... 18 A/mm2; - heating temperature - 1000-1050 °C (for austenitization); - heating time - 40 seconds (determined by the current density); - tension - – S·σsк, where S - the coefficient that determines the desired regime of tube stretching, σsк - resistance to deformation at the maximum heating temperature tк (S the coefficient can be set in range from 0 to 1); - external cooling by air or water. 4.
"Work is made as part of the public task in the field of scientific activity № 11.1369.2014 / K on 07/18/2014 (state registration number: 114122470051)" LITERATURE [1] BAKIROV M.B., KLESHHUK S.M., NEMYTOV D.S.

The remaining part is used as an active filler, because the silica fume particles are approximately 100 times smaller than a grains of cement [4].
Therefore, they are able fill in the space between larger grains and thereby contribute to increasing the overall density of the concrete.
This is caused mainly by the aforementioned pozzolanic reaction (1), but also by increasing the density as a result of filling the space between the grains of cement.
The total number of produced mixtures was 11.

Table 1 The parameters of the vacuum hot-pressing diffusion welding Sample Number Temperature [K] Pressure[MPa] Holding Time[h] Aluminium Sheets Atmosphere 1 833 6 1.5 4mm/Cold rolling Argon 2 833 6 2 4mm/Cold rolling Argon 3 833 6 2.5 4mm/Cold rolling Argon 4 853 6 2 4mm/Cold rolling Argon 5 873 6 2 4mm/Cold rolling Argon 6 873 6 2 4mm/non-Cold rolling Argon Then, the composite sheets were cut into 10×10mm square pieces，cross-sections of the annealed diffusion couples were examined by SEM and EDS and the sides of Titanium were examined by using electrochemical workstation.
Fig.2(5)and(6) show the SEM images of Ti-Al interface held at 873K for 2h respectively under the pressure of 6MPa.The thickness of diffusion interface layer with aluminum sheets by cold-rolling(1.25µm) is thicker than non-cold rolling(924nm).In general, Grain-boundary diffusion coefficient(DB) is greater than volume diffusion coefficient (DL)[5].Grain of aluminum sheets by cold-rolling are refined.
Then,it produces a large amount of grain boundaries and dislocation and provides fast channel for the diffusion of atomic.

Nucleation and coarsening process of cementite was not completed after GA process simulation, suggesting that the number of fine carbides was higher after the GI cycle simulation.
In case of as-quenched martensite, the main contributions are; intrinsic lattice friction, solid solution effect of interstitial carbon, fine grain size and the interaction between dislocations.
After tempering, by contrast, it was reported that grain size dependence of strength disappeared, even though tempering process did not change the high angle boundary structure of martensite.
Flat flow curves have also been reported in ultra fine grained materials [5], both in the steel and in pure Al systems.

However, a large number of cracks and porous can be observed in these coatings after oxidation and the coarse grains have negative influence on the surface roughness and properties of alumina coatings.
And the grains of coatings are refined, forming nano-crystals [6].
Combined with Figure 3(c) and (d), it is found out that a relative fine-grained surface of Al coatings is tend to form more α-Al2O3 after plasma oxidation.

The laterite soil material contains 59.96% iron compound FeO [3], a brown-to-yellow, fine-grained, light-textured, nodular-grain, well-cemented brick-like soil [2].
And every behavior and changes in mechanical properties were then observed Table 1 Mix Design Num Mix (%) Number of Sample for Unconfined Compressive Strength and California Bearing Ratio Total Sample Laterite Soil Zeolite Water glass Curing Times 0 Day 7 Days 14 Days 28 Days S1 94 4 2 6 6 6 6 24 S2 90 8 6 6 6 6 24 S3 86 12 6 6 6 6 24 S4 82 16 6 6 6 6 24 S5 79 20 6 6 6 6 24 Results and Discussion Fig. 1 Micro Spectrum of XRD test on Laterite soil Table 2 Chemical Components of Laterite Soil Chemical Components Molecular Formulation % Aluminum Al2O3 17,72 Silicon SiO2 19,15 Titanium TiO2 3,00 Iron FeO 59,96 Potassium K2O 0,05 Magnesium MgO 0,12 The chemical components of the laterite soils consist mainly of 59.96% iron dioxide and 19.72% silicon dioxide, followed by 17.72% aluminum.
The grains dominated by silt 58,10%.