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As the low heat conductivity of titanium alloy, a large number the heat are concentrated in the tip and the blade under the dry continuous cutting condition, which caused the cutting edge softening and deformation when the hot crack developed to a certain extent, it produced a dramatic phenomenon of tool breakage failure.
When the bonding friction surface has relative motion, the grain or grain groups, which have been cut away due to the tension caused by adhesive wear of the tool.
From the Figure 3(b)it can be seen that there are a large number of oxygen element in the A position.

Fig. 4a,b: Ultrasonic wave velocity according to temperature and exposure time for PP fiber mortars (on the left) and for GL fiber mortars (on the right) Thus, of the same feature curves are appeared also for a number of measured and calculated quantities as for bulk density, tensile and compressive strengths, tensile and compressive Young R T l=160mm 0 500 1000 1500 2000 2500 3000 3500 4000 4500 5000 0 100 200 300 400 500 600 700 800 900 100 0 T (oC) c (m/s) PP / 10min PP / 30min PP / 60min PP / 120min 0 500 1000 1500 2000 2500 3000 3500 4000 4500 5000 0 100 200 300 400 500 600 700 800 900 100 0 T(oC) c (m/s) GL / 10min GL / 30min GL / 60min GL / 120min modulus, first crack stresses.
These variations have to do with a number of physico-chemo-mechanical changes that take places in gas, hydro and solid phases of mortar constituents and products.
The calcium hydroxide that found in hardened mortars in huge quantities, comes by the hydration process of cement grains during the curing period.
A further temperature enhancement to 900o C, leads to a total destruction of the mortars due to the fact that in this temperature levels the calcium carbonate the main constituent of marble grains is decomposed, leading to very low strengths up to only 10% of the initial ones, whereas at 400 o C the appearing strength reduction was only 30%.

In regions where the dispersoid number density is low, the alloy may therefore still be prone to recrystallisation.
Investigations of the grain structure in the profiles were performed on polished and anodised samples in the longitudinal section.
Recrystallised grains are randomly distributed through the thickness of alloy 4 after annealing of profiles cold deformed 0%, 10% and 20% at 600ºC.
The highest resistance towards recrystallisation, however, was obtained in the Sc+Zr-containing alloy 5 which contains no primary phases and a high number of homogeneously distributed and thermally stable Al3(Sc,Zr)-dispersoids [3,6].

However, Liao et al [5] found that the modification of Al-Si alloys with Sr addition increased the size of the eutectic grains and reduced the number of eutectic grains.
Table 1 Orthogonal test results of Al-40Si alloy modified by 1.0 wt% Sr addition Number Solution temperature Ts [℃] Solution time ts [h] Aging temperature Ta [℃] Aging time ta [h] Hardness [HRC] 1 450 10 160 5 15.7 2 450 14 200 7 17.1 3 450 18 240 9 15.1 4 500 10 200 9 14.8 5 500 14 240 5 15.0 6 500 18 160 7 16.2 7 550 10 240 7 13.6 8 550 14 160 9 19.1 9 550 18 200 5 20.6 According to the range analysis method, the influence of each factor on the hardness is analyzed and the optimal condition is obtained.

Smooth surface and columnar grains were observed in Fig.3.
The columnar-grained structure was related to the preferential growth of the hexagonal structure of ZnO, which is consistent with the XRD analysis.
Fig. 8 shows variations of HRS and LRS resistances as a function of cycle numbers of Cu/ZnO/ITO device.
Variations of HRS and LRS resistances as a function of cycle numbers of the Cu/ZnO/ITO device 4.

Tab.1 Influence on of pore structure parameter specimen number FA FAC 1 2 3 4 5 6 1.6 0．19 0.0601 0.1325 0．22 0.0555 0.1040 0．32 0.0532 0.0857 2.5 0．22 0.0432 0.0786 1.6 0.0555 0.1040 0.9 0.0598 0.1139 Tab.2 Influence on of the excitation frequency frequency [Hz] FA FAC 30 0.0623 0.1041 50 0.0619 0.0939 100 0.0609 0.0888 200 0.0598 0.0976 400 0.0589 0.1432 500 0.0555 0.1040 700 0.0518 0.0953 800 0.0475 0.1009 900 0.0412 0.1279 1000 0.0432 0.0952 Fig.3 Fitting curve Fig.4 Fitting curve Fig.5 Fitting curve of FA and FAC of FA and FAC of FA and FAC For clarity, data in table 1 and table 2 are fitted corresponding FA and FAC/ epoxy composite 、 and curve which are shown in Figure 3 ~Figure 5.
The relationship equation between foam internal friction and frequency, porosity and pore size can be derived by the law of plane wave [6]: (1) Where is the internal friction of elastic wave, is the internal friction in volume fraction, is shear wave velocity, is expansion wave velocity, and are respectively the wave velocity that the volume fraction changes in high and low frequency, can reflect the strength of changes coupling between displacement and the volume fraction, is macroscopic density, is balance inertia (inertial measurement of volume fraction changes), is the damping coefficient in volume fraction changes, is "diffusion" coefficient in the volume fraction changes, is frequency, is porosity, is pore radius, is radius increment on the boundary of hole, is the number of holes per unit volume.
Ledermen inducted a mathematical formula about interface slippage damping [8]: (2) Where, ,is friction coefficient between interfaces, is radial stress concentration factor in interfaces, is the volume content of the grains.
For FAC, the volume content of the grains should be the porosity of FA, .

The results showed that micro-hardness, porosity and compress strength of Cu-Al2O3 materials increased with increasing of Al2O3 content, which was the result of dispersion of the fined Al2O3 grains in Cu-matrix.
The results showed that micro-hardness, porosity and compress strength of Cu-Al2O3 materials rised with increasing of Al2O3 content, which were the results of dispersion of the fined Al2O3 grain sizes in Cu-matrix.
Acknowledgements The work described in this paper was supported by the Science and Technology Fund of Thai Nguyen University (TNU) for the Grant number DH2014-TN02-04 project.

（show in table 1） Table 1 Orthogonal experiment table Test numbers Density (g/cm3) Pressing time (min) Pressing temperature (℃) 4 1 1(0.75) 1(12) 1(130-140) 1 2 1(0.75) 2(15) 2(145-155) 2 3 1(0.75) 3(18) 3(160-170) 3 4 2(0.85) 1(12) 2(145-155) 3 5 2(0.85) 2(15) 3(160-170) 1 6 2(0.85) 3(18) 1(130-140) 2 7 3(0.95) 1(12) 3(160-170) 2 8 3(0.95) 2(15) 1(130-140) 3 9 3(0.95) 3(18) 2(145-155) 1 Orthogonal experimental results of Bamboo plywood are shown in Table 2: Table 2 The main physical and mechanical properties of bamboo plywood Ply bamboo Thickness Moisture content Density 24hTS MOR MOE 2hIB mm % (g×cm-3) % Parallel to grain Stripes Parallel to grain Stripes MPa 1 12 10 0.75 3.3 109.7 53.5 9681 5603 0.86 2 12 10 0.75 3.3 129.7 60.2 11362 5650 1.03 3 12 10 0.75 3.3 139.7 91.9 17420 10296 1.36 4 12 10 0.85 4.2 129.9 79.8 8287 5031 1.17 5 12 10 0.85 2.3 139.4 94.3 16749 11353 1.40 6 12 10 0.85 3.0 118.5 75.2 7738 5205 1.22 7 12 10 0.95 3.0 138.5 95.3 16645 10801 1.35 8 12 10 0.95 4.2
115.2 74.4 7178 4955 1.30 9 12 10 0.95 3.0 100.1 74.9 5426 5969 1.30 EN300-2006 6~8 12 30 16 4800 1900 0.17 OSB/4 10~18 12 28 15 4800 1900 0.15 Requirements in the JG-T 3026-1995 bamboo plywood formwork is listed in Table 3 Table 3 The performance of ply bamboo Number Project Unit Superior product First grade Qualified products 1 Density g/cm3 ≥0.85 ≥0.85 ≥0.85 2 Moisture content % ≤12 ≤14 ≤15 3 Water absorption % ≤12 ≤14 ≤17 4 MOR ∥ N/mm2 ≥7×103 ≥6.5×103 ≥6×103 ⊥ N/mm2 ≥5×103 ≥4.5×103 ≥4×103 5 MOE ∥ N/mm2 ≥90 ≥80 ≥70 ⊥ N/mm2 ≥60 ≥55 ≥50 As shown in table 2, the value of MOR and MOE in experiment group No.3, 5, and 7 is twice more than other groups.

Rudd et al. [4] formulated a coarse-grained molecular dynamics (CGMD) method, derived directly from finite temperature MD through a statistical coarse graining procedure.
According to the meshfree method, the continuum domain can be represented by finite number of nodes.
The number of interpolation points, evenly distributed in the bridging domain, is 35.

Furthermore, the conventional sintering of HA ceramics requires long time and high temperature, which produces a grain size greater than that of bone apatite crystal, reduces the bioactivity and bioresorbability [4].
In ceramic bodies there is strong dependence between microstructural parameters (such as pore volume/shape and grain size) and mechanical properties.
For all samples, increase in number of viable cells is observed by elapsing culture time.
No significant difference is observed between the number of proliferated cells on control group and sintered samples at all culturing periods.