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Also, the number of peaks in the X-ray diffractograms increases with increase in thickness of the films.
The data presented in table 1 shows a good agreement with the standard data seen in JCPDS (15-0746) [17] for cubic structure of ZnTe.
Thickness [h k l] Lattice constant a [Å] 2θ Degree Grain size D [Å] Micro strain ε 10-3 [lines-m2] Dislocation density ρ 1015 [lines/m2] Lattice spacing d [Å] XRD JCPDS 6kÅ (1 1 1) 6.1170 25.21 25.27 246.974 1.4656 1.6393 3.5310 8kÅ (1 1 1) 6.1193 25.20 25.27 246.979 1.4658 1.6394 3.5330 10kÅ (1 1 1) 6.1115 25.24 25.27 246.990 1.4657 1.6392 3.5280 Optical analysis.
Interestingly, it is observed that with increase in thickness of the films, the number of additional peaks (fig. 2) increases before the fundamental absorption edge.
[18] JCPDS International centre for Diffraction Data, USA, (1997) Card No.15-0746

All of the powder XRD patterns were assigned to the langasite-type phase by the comparison to the crystallographic data of the corresponding langasite phases in JCPDS cards, meaning that the langasite-type phases could be formed by the crystallization of the glasses without introducing of any impurity phases.
The Raman bands around 860 cm-1 and 540cm-1 are attributed to the GeO4 tetrahedra with and without NBO, respectively (i.e., the Ge at D and C site). [11,12] The band at ∼400 cm-1 is probably related to the vibration of Ca (Sr)-O bond (i.e., corresponding to the band for A site). [7] In addition, since the Raman band around 810 cm-1 is ascribed to the antisymmetric stretching vibration of Ge IV -O-Ge VI (Superscript of Roman numeral indicates the coordination number), [13] the small bands around 800 cm-1 is probably due to the presence of octahedral GeO6 units in the NCG and NSG phases.
Intensity (arb. units) (JCPDS:67-2064) �CG glass PGG glass Figure 1 Powder XRD patterns of langasite-type phases crystallized in the corresponding glasses. 400 600 800 1000 1200 Wavenumber / cm -1 Intensity (arb. units) PGG glass �CG glass �SG glass Figure 2 Raman scattering spectra of the crystallized langasite-type phases (solid line) and the as-quenched glasses (dashed line).

It can be found that the XRD patterns of all samples are similar to each other, and all detected diffraction peaks for Sr3Lu1–x(PO4)3:xDy3+ within the whole range of Dy3+ doping contents are well indexed to the standard data of Sr3Lu(PO4)3 with JCPDS card No. 33-1344.
Fig. 1 XRD patterns of Sr3Lu1–x(PO4)3:xDy3+ (x = 0.02, 0.04, 0.06, 0.08, 0.10) phosphors and JCPDS No. 33-1344.
Based on the report of Blasse, the critical transfer distance (Rc) is approximately equal to twice the radius of a sphere with the volume: (1) where V is the volume of the unit cell, xc is the critical concentration of activator ion, and N is the number of cations in the unit cell.

The crystallization of the ZnO hexagonal phase with a wurtzite structure and the ZnAl2O4 phase with a cubic structure occured according to (Joint Committee on Powder Diffraction Standards (JCPDS) PDF numbers 00-036-1451 and 01-073-1961 respectively) is noted.
The TC(hkl) values of our film (see Table 1) are calculated using the following formula [25]: (1) Where I(hkl) and I0(hkl) are respectively the relative intensity of the (hkl) peak and the standard intensity of the (hkl) peak given in the JCPDS cards, n is the number of diffraction peaks.
ZnO nanostructures can typically have a number of defects such as oxygen vacancies, lattice disruptions, etc.
From the figure 7(a) it is noticed that some diffraction peaks agree well with the standard pattern of ZnO phase (JCPDS card No. 36-1451), reflecting the (002) and (101) planes.
The peaks position are found well matching with those of the standard pattern of a-Zn2SiO4 (Rhombohedral crystal structure with an R3 space group, lattice parameters, a = b = 13.9381 (Å) and c = 9.3100 (Å), JCPDS card No. 37-1485).

The results shown that glass ceramic phase is CaNb2O6, grain size is about 30 nm, The two-stage controlled heat treatment is beneficial to control of the number and size of grains, thus affecting the transparency of glass ceramic and luminescence properties.
As can be seen from the fig.2, the XRD diffraction spectrum of the sample diffraction peak Comply with JCPDS card CaNb2O6 the standard diffraction peaks.
Changes of particle size and distribution are evident along with the extension of heat treatment temperature. heat treatment temperature on the morphology control of microcrystalline glass is very important, with the extension of heat treatment temperature, the grain number increase gradually.

A number of excellent reviews have been published recently.
There is a clear growth in waste generation in recent decades, mainly in the mineral sector, with large numbers in various types and levels of dangerousness.
Chemical composition Al2O3 SiO2 SO3 Na2O Oxides (%) 95.8 1.7 1.6 0.8 According to Figure 11, the results of the x-ray diffraction of the Bayer process alumina residue indicates the presence of gibbsite (Al(OH)3) as predominant phase (JCPDS 74-1775) and α-alumina (JCPDS 10-0173).
Figure 16 - Particle size distribution of the ceramic mass with alumina residue From the X-ray diffraction curves of the ceramic mass (Figure 17) it was showed the presence of the crystalline phases of gibbsite (standard card PDF 74-1775), α-alumina (standard card PDF 10-0173), kaolinite (standard card PDF 29-1488), smectite (standard card PDF 29-1497) and quartz (standard card PDF 46-1045).
After sintering at 900, 1000 and 1100 °C, it was observed the presence of α-alumina, mullite (standard card PDF 15-0776) and cristobalite (standard card PDF 39-1425).

Characteristic peaks are observed for all diffraction patterns, which are indexed to the standard card (JCPDS card no. 36-1451).
Table 1　Factors and levels of orthogonal experiment Level Air Access Amount(mL/min) Catalysts Addition Amount (g) Photoirradiation Time(h) 1 10 0.015 1.0 2 30 0.020 1.5 3 50 0.025 2.0 Table 2 Orthogonal experiment results Experiment number Air Access Amount (mL/min) Catalysts Addition Amount (g) Photoirradiation Time (h) Desulfurization Rate (%) 1 1 1 1 76.8 2 1 2 2 87.2 3 1 3 3 82.2 4 2 1 3 78.1 5 2 2 1 70.6 6 2 3 2 94.4 7 3 1 2 85.1 8 3 2 3 80.6 9 3 3 2 75.1 K1 246.2 239.0 222.5 K2 243.1 238.4 266.7 K3 240.8 251.7 240.9 k1 82.1 79.7 74.2 k2 81.0 79.5 88.9 k3 80.3 83.9 80.3 R 1.8 4.4 14.7 Conclusion The Photo-Cat-ODS of simulation gasoline (thiophene dissolved in n-octane) with WO3/ZnO as catalysts and O2 as oxidant was optimized by orthogonal experiments.

All the anatase structure of TiO2 diffraction peaks can be found in No. 84-1286 card, rutile structure of TiO2 indexed in No. 86-0147 card, wurtzite structure of ZnO indexed in JCPDS card No.80-0075 and cubic phase of ZnTiO3 were well matched with JCPDS card No. 39-0190.
In this test the amounts of colonies are steady and after one hour the number of the bacteria colonies decreases and it takes some time for reactive species reach to the faraway bacteria.

Figure 1 XRD of Silver nanowire Figure 2 EDS of the Silver nanowire All the diffraction peaks in the 2θ range measured corresponds to the FCC structure cubic of Silver with lattice constants a = 4.068Å and are in good agreement with those on the standard data card (JCPDS card No. 87-0719).
As the reaction mixture was refluxed at ~160 °C, the number and length of these nanowires increased over a period up to ~60 minutes.

The JCPDS-International Centre for Diffraction Data Cards were used as a reference. 2.4 Structural analysis of bioactive glass by FTIR Reflectance spectrometry The structures of biocomposite samples were measured at room temperature in the frequency range of 4000–400 cm−1 using a Fourier transform infrared spectrometer, (Bruker Tensor 27 FTIR,USA).
XRD patterns of these samples show that the main phases are pseudowollastonite and hydroxyapatite (JCPDS No.: 090432).
To compare the intensity of the formed phases, two characteristic peaks of pseudowollastonite (JCPDS No.:19-0248) and hydroxyapatite were selected for comparison. 2θ = 36.80 for wollastonite and 2θ = 40.17 for hydroxyapatite phase were selected and their intensities were compared.
It is proposed that the larger addition of glass gives a larger number of ions present, and these ions enter the HA structure and become interstitial ions. 3.2 pH behavior in SBF The variation in pH values of simulated body fluid (SBF) after soaking of biocomposite for various time periods is shown in Fig. 6.