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In recent times, a number of methods have been developed to create nanostructures of CeO2 that are considerably various from the techniques used for producing bulk materials, such as ball milling [5], hydrothermal [6], sol-gel [7], and so on.
On the other hand, when various calcination temperatures are applied to the sample, the crystalline behaviour of the sample becomes visible with peaks indexed by (111), (200), (220), (311), (222), (400), (331) and (420) planes (JCPDS card no. 34-0394), which are in turn ascribed to the cubic fluorite structure and lattice parameter of a=5.4113 Ǻ.

Figure 2 shows that all yttria obtained are cubic phase(JCPDS card 41-1105).
Large number of nuclei and small grains may be obtained in the early stages of amorphous yttria converted to cubic yttria, in which the nuclei and small grains are closely interdependent.

These results are in good agreement with standard ZnO (JCPDS card No. 36-1451).
In the case of the 3% Ag/ZnO sample, an additional small peak at 2θ=38.8º marked with “*” is also created which is related with the face centered cubic phase of metal Ag NPs according to (JCPDS file No. 04-0783) [3], [12].
From eq. 2, increasing the numbers of ZnS molecules will lead to an increase in the sensitivity and the recovery time, while the response time will decrease because in desulfurization process ZnS molecules should be changed into ZnO again, according to Mortezaali and Moradi [23] and the following reaction: 2ZnS(s) + 3O2(g)desulfuration 2ZnO(s) + 2SO2(g) (3) Fig. 9.

Fig.1 shows the XRD patterns of Sc0.88Lu0.05(V0.5P0.5)O4:Eu3+0.07 (a), Sc0.88Lu0.05(V0.8P0.2)O4:Eu3+0.07 (b), Sc0.88Lu0.05(V0.9P0.1)O4:Eu3+0.07 (c), Sc0.88Lu0.05VO4:Eu3+0.07 (d) and the standard card of ScVO4 (01-082-1967).
We can see that compared with the standard card of (01-082-1967), the diffraction peaks of Sc0.88Lu0.05(V1-xPx)O4:Eu3+0.07(x=0,0.1,0.2,0.5) samples were completely the same, and the three strong peaks were come from the crystal diffraction of (200), (112) and (312), respectively.
Fig. 1 X-ray powder diffraction pattrens of Sc0.88Lu0.05(V0.5P0.5)O4:Eu3+0.07 (a), Sc0.88Lu0.05(V0.8P0.2)O4:Eu3+0.07 (b), Sc0.88Lu0.05(V0.9P0.1)O4:Eu3+0.07 (c), Sc0.88Lu0.05VO4:Eu0.07 (d) and JCPDS data for ScVO4(01-082-1967) Fig. 2 The lattice constant d of Sc0.88Lu0.05(V1-xPx)O4:Eu3+0.07 decreased linearly with the increase of x Table 1 XRD data and cell parameters of Sc0.88Lu0.05(V0.5P0.5)O4:Eu3+0.07, Sc0.88Lu0.05(V0.8P0.2)O4:Eu3+0.07, Sc0.88Lu0.05(V0.9P0.1)O4:Eu3+0.07 and Sc0.88Lu0.05VO4:Eu0.07 Composition Cell parameter (200) (112) (312) a/nm c/nm V/nm3 Sc0.88Lu0.05VO4:Eu0.07 26.10 34.53 51.69 0.68031 0.61473 0.28451 Sc0.88Lu0.05(V0.9P0.1)O4:Eu3+0.07 26.39 34.68 51.77 0.68694 0.61073 0.288195 Sc0.88Lu0.05(V0.8P0.2)O4:Eu3+0.07 26.44 34.75 52.87 0.68237 0.60853 0.283349 Sc0.88Lu0.05(V0.5P0.5)O4:Eu3+0.07 26.62 35.83 52.96 0.67828 0.60416 0.277952 Morphology analysis.
When the PO43- doping concentration is 0.2, the fluorescence lifetime of the sample reaches maximum number of 0.4805ms.

The energy band gap decreases with increasing number of layers but increases with increasing pre-heating temperatures.
Structure analysis The XRD patterns of the ZnO thin films (Fig. 2), as can be seen from (Fig. 2a), all detectable peaks can be ascribed to the ZnO Zincite-type structure (JCPDS card No. 01-073-8765).
Grain growth occurred along the (002) plane for all films irrespective of sol concentration, aging time or number of layers.
From Fig.5b, it can be clearly observed that the transmittance increases with increasing number of layers, with a peak value of 90%.
Taking into account the effect of the number of layers, the film with 10 layers pre-heated at 400°C is the thicker one.

The 2θ values of 25.50, 31.41, 33.20, 39.43, 46.82 and 49.68 obtained correspond to HAp (002), (211), (222), (212), (222) and (213) reflection planes respectively and they are in good accord with the standard JCPDS card # 09-0438.
The incorporation of fluorine into the HAp matrix is conveyed by a small shift in the XRD patterns of apatite phase screening close with fluorapatite and is in good accord with the standard JCPDS card # 71-0880.
The process of apatite formation mainly depends on the negative group, which in turn depends on the large number of negative ions (i.e.
As the soaking time increases from 7 to 28 days, there is a corresponding increase in the number of agglomerated particles both for HAp and F-HAp which indicates enhanced bioactivity.
The number of live (80%) and dead (20%) cells are almost the same on both PCL and F-HAp coatings on 316L SS.

XRD patterns for BaYF5:Yb3+, Er3+ precursor (a), BaYF5:Yb3+, Er3+ obtained by sintering the precursor at 600°C temperature (b), and the JCPDS card 46-0039 for BaYF5 is also given.Synthesis and molecular structure of the UV-curable sealant.
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The JCPDS card number and XRD readings (00-006-0464) were compared.
Figure 2 displays all diffraction peaks corresponding to (220), (311), (222), (400), (422), (511), (440), (533), and (622) planes in the XRD pattern, which were indexed with the standard ZTO spinel cubic structure (JCPDS #24-1470) data.
Reduced particle size results in a larger surface area available for interaction with bacterial cells due to the higher number of surface atoms.

The characteristic of peak of Cr metal (JCPDS card No 06-06394) lays on d110 (Figure 2).
Transmittance (a.u) Wave number (cm-1) Fig. 2.
The number of acid site in this research was the total acidity that included Lewis and Brønsted acid.
The presence of oxide metal of ZrO2 and Cr metal on the surface of catalyst will increase the number of active sites at the surface of catalyst (Table 2).
The number of acid site is affected by the properties of pillar and condition in synthesis such as reflux’s temperature and mole amount of pillaring agent [19, 20].

There are a number of physical methods for preparing nanomaterials viz. inert gas condensation, physical vapor deposition, laser ablation, chemical vapor deposition, sputtering, Molecular Beam Epitaxy etc.
This change in behavior is also explained by number of C, H and O molecules available during the combustion for various ratios.
In citrate-nitrate combustion, since more number of gases are evovled the combustion temperature reaches to maximum value very slowly compared to glycine.
Thus in citrate-nitrate combustion number gas molecules evoveled dominates over the flame temperature.
The CuO nano particles give the pure monoclinic structure (JCPDS card files of CuO (80-1917)) with lattice parameters a = 4.68 Å, b = 3.42 Å and c = 5.12 Å and are in good conformity with the reported data.