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The FT IR spectra of the gel dried at 100 ºC was measured by using a Jasco-FT/IR-4100 spectrometer in the wave number range 4000-400 cm-1 using 70 scans for each sample.
This decrease in crystallite size may be due to the distribution of dopant cations at the crystal lattice or it may be on the grain boundary of TiO2 which inhibits grain growth by providing a barrier between the TiO2grains[18].
In addition to this the decrease in crystalline size may attributed to the presence of Ti-O-Sm bond formation in the Sm3+ doped sample, which inhibits the growth of crystal grains[19].
This higher surface area of Sm3+ doped TiO2 can help to absorb more number of dye molecules compared to bare TiO2 during the photocatalytic reaction and hence contribute towards higher photocatalytic effiency. 3.4 Scanning Electron Microscopy (SEM) The morphology of the TiO2 and Sm3+ doped TiO2 sample was analyzed using Scanning Electron Microscopy (SEM).
The average grain diameter was measured as being in the range of a few nanometers.

In Mg-6Zn-1Ce alloy (Fig. 4a) alloy the average grain size of α-Mg is about 30 μm and area fraction of intermetallics is about 3.8%.
In Mg-6Zn-2Ce alloy the average grain size of α-Mg is about 27 μm and area fraction of compounds is about 5.0%, as shown in Fig. 5a.
Discussions Due to the low addition of Ce, there are still a small number of Mg4Zn7 and Mg7Zn3 phases in Mg-6Zn-0.6Ce alloy.
When the additive amount of Ce in Mg-6Zn alloy increase to 1%, the main compound in Mg-6Zn alloy is the Mg-Zn-Ce phase and a small number of β1′ precipitation particles in matrix.
Buha, Grain refinement and improved age hardening of Mg-Zn alloy by a trace amount of V, Acta Mater. 56 (2008) 3533-3542

The performance of CrN/TiN multilayer coatings was found to be associated with the modulated period (Λ), grain size, and interface structure [17, 19-21, 25-27].
The thicknesses of NML structures were measured by a Calotest using a steel ball with a diameter of 30 mm and a diamond paste with 0.1µm monocrystalline diamond grains.
This is probably due to follow effects: decrease of the modulation period leads to decrease of crystallite size, and leads to the increase of the hardness according to the Hall-Petch law (H ~ d-1/2, d is the grain size).
SGS-2022-5060 and by the project “Pretreatment, coating and protection of the substrate”, registration number CZ.01.1.02/0.0/0.0/20_321/0025264 were obtained through the financial support of the Ministry of Industry and Trade in the framework of the targeted support of the “Application VIII”, the Operational Programme Enterprise and Innovations for Competitiveness.
Aoki, Coefficients of friction of TiN coatings with preferred grain orientations under dry condition, Wear 265 (2008) 1017–1022

Introduction Magnesium alloys have excellent physical and mechanical properties for a number of applications.
There is a number of technologies available for coating magnesium alloys.
After anodizing, the following investigations were carried out; surface morphology, grain size of the anodic film, analyzing the phases in the anodic coating, corrosion testing, the anodic film thickness, adhesion of the anodic film, and microhardness measurements [15].
The results indicated the presence of amorphous and some nano crystals with an approximate grain size of 3 to 5 nm before heat treatment which increased to 30 to 50 nm after heat treatment (HT).
First stage: deformation of surface asperities by plastic flow and creep (Figure 9-a), second stage: grain boundary diffusion of atoms flow to the voids and grain boundary migration (Figure 9-b) and third stage: volume diffusion of atoms to the voids.

The dimensions of the blank wallboard without flame retardant (Grain board) are 460×460×1.5 mm, the default density is 6.5 g/cm3.
The measurement of flame retardant properties (oxygen index), was determined using<>.[11] Experimental results and analysis The effects of Al(OH)3 single-component flame retardant system on wallboard properties.Table 2 shows the experimental results for the properties of the flame retardant wallboard and grain boards containing different levels of Al(OH)3.
Compared to the grain board without flame retardant, its internal combinative strength decreases 58.9% at most, and decreases more rapidly.
Results for the single-component Al(OH)3 flame retardant system Wt. % Al(OH)3 Density [g/cm3] Water ratio % (2h) % Water absorption Inside combinative strength [MP] Oxygen Index Formaldehyde Release 50% 0.708 5.9 61.0 1.53 0.089 30.0 E0 60% 0.720 6.1 59.6 1.49 0.075 31.8 E0 70% 0.744 5.7 55.9 1.47 0.068 33.0 E0 80% 0.761 6.1 50.1 1.10 0.053 34.4 E0 Blank control 0.645 7.7 70.5 1.76 0.129 24.4 E0 With increasing amount of Al(OH)3, the bibulous ply inflation rate of the flame retardant wallboard decreases, but decreases less than that of the grain board.
Orthogonal experimental extreme difference analysis of comprehensive evaluation for multi-component fire retardant system Number Factors and levels A B C Comprehensive evaluation 1 1 1 1 0.5829 2 1 2 2 0.5852 3 1 3 3 0.7594 4 2 1 2 0.5236 5 2 2 3 0.7822 6 2 3 1 0.6467 7 3 1 3 0.7047 8 3 2 1 0.5393 9 3 3 2 0.5351 Average 1 0.642 0.604 0.590 Average 2 0.651 0.636 0.548 Average 3 0.593 0.647 0.749 Extreme difference 0.058 0.043 0.201 Ideal composition A2 B3 C3 Repetitive experiments for group optimization and contrast analysis.

The yield stress σy of a single phase material is calculated using the standard Hall-Petch equation: 1/2 y y0 gkd− σ = σ + (1) where σy0 and k are the intrinsic flow stress and Hall-Petch coefficient of that phase both of which are composition dependent, and dg is the grain size.
The most critical factor was found to be the APB energy, which is obtained from a thermodynamic calculation route described previously.[15] Calculations have been made for a number of commercial superalloys where detailed information on γ' particle size is available, Fig. 3.
The total number of γ' and γ" particles is kept constant, which means that they shrink in size with increasing temperature.
Using the reported average grain size 50 µm and particle size 40 nm,[41] the room temperature yield strength of the alloy is calculated as 785 MPa.
Using the observed precipitate size 100 nm with a grain size of 175 µm, the calculated room temperature yield strength is 774 MPa and γ' particle size back Fig. 7.

As a result, it was shown that introducing Si improves the strength of the interface (and the composite material in general) for different grain orientations.
Extensive studies were carried out on the sliding at metal/metal interfaces with same material (grain boundary) in Al [6, 7], Cu [8] and Ni [9] or different materials of Ni/Zr [10], Ta/Al, Cu/Ag [11].
The critical shear stress (CSS) was calculated based on applied force (fi) and number of atoms in moving zone (N) and the cross-sectional area of a layer (S) (Eq. 1). ⋅= ∑=S f N i i 1τ (1) The threshold of applied forces for initiating sliding at the interface was determined for various Al/Si interfaces with different alignments and orientations.
However, the applying shear force causes inter-granular sliding between two mis-oriented Al grains, without any distortion of the lattice at the Al/Al interface nor inside the Al.
Number of non-three-atom rings in Al before and after sliding for 5, 10, 15, 20 and 25 ps, 10 Å regions near the interface was considered. 0 1 2 3 4 5 6 7 1 2 3 4 5 6 Region_1 Region_2 Region_3 Displacement (Å) Time (ps) a) 0 0.2 0.4 0.6 0.8 1 1.2 1 2 3 4 5 6 Region_1 Region_2 Region_3 Displacement (Å) Time (ps) b) Figure 5.

According to the characteristic of wind-blown sand movement the sand grains phase and the gas phase are modeled by considering the different kernel function and the particles size, mass, density, velocity and other physical quantities, which can movement along with controlling equation.
Then the Eq. 2 can finally be written as (6) where N is the number of particles within the support domain of particle.
Some particles shows saltation movement resembled as parabola, as particles of number 1, 2, 4 and 6; and some particles shows suspending movement in a higher altitude than others, as particles of number 3 and 5, and some others moving on a horizontal line likes creeping movement on the ground surface, as particles of number 7.

The reaction is a liquid-liquid reaction; the generated zinc molybdate has very fine grains and can be hardly centrifuged.
And the results are shown in Fig. 6 and Fig. 7: Fig. 6 X-ray diffraction graph of zinc Molybdate synthesized by double decomposition with sodium molybdate Fig. 7 X-ray diffraction graph of zinc Molybdate synthesized by ammonium heptamolybdate method Using the patterns above, we did retrieval and analysis in the database of X-ray diffraction patterns and the results are as follows: Zinc molybdate by sodium molybdate method: molecular formula NaZn2OH(MoO4)2H2O(card number：70-0161), belonging to the monoclinic system, space group C2/m Corresponding cell parameters: a=9.436 Å b=6.338?
c=7.679 Å β=115.80 Å Zinc molybdate by ammonium heptamolybdate method: molecular formula H3NH4Zn2Mo2O10 (card number：73-2389), belonging to the trigonal system, space group: R3m.

Disruption of the sample was caused by exceeding of timber strength in tension perpendicular to the grains, but a block shear collapse was not observed.
There were achieved various number of loading cycles (3 – 120000).
There can be seen trend of the relationship between carrying capacity of the joint loaded by dynamic forces (Fdyn) and carrying capacity of the joint loaded statically (Fstat) – Frel - in dependence of number of loading cycles: (1) Fig. 4: Results of dynamic loading round timber joints tests During dynamic testing (by multicycling passing loading) smaller part (one third) of tested samples failed in different way in opposite to static tests – by block shear (see Fig. 5).