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For all the final products at different reaction parameters, the formation of the pure covellite of CuS with hexagonal phase has been confirmed with the JCPDS data.
All diffraction peaks were closely indexed with the standard peaks of CuS hexagonal phase with JCPDS card no. 04-0464 and the cell parameters are a=3.792 and c=16.344.
The XRD graph clearly show peaks at (101), (102), (103) (008), (110), (108) and (116) as in accordance with the JCPDS file indicating that CuS exists as covellite phase.
In the case of 24 hrs reaction time, a number of additional peaks were observed than compared with 5 hrs reaction time.

In order to establish the relationship of ZnO morphology and photocatalytic performance, still need to base a large number of experimental studies lay the foundation for the theory system.
As can be seen from the graph, all peaks match the peak of Zinc Carbonate Hydroxide on standard card (JCPDS 19-1458), the precursor with this method for the synthesis is Zinc Carbonate Hydroxide.
All peaks in B diagram (JPCDS 16-3451) is exactly the same as all peaks of Zinc Oxide Standard card, and did not detect other miscellaneous peak, that after firing, precursor into the Zinc Oxide.

The patterns are identical with JCPDS Card No.80-1900, which shows a tetragonal phase (b).
From the high magnification image inset Fig. 2a, we can find that the as-prepared La2S3 microcrystalline is composed of a large number of flakes-like structure.
From high magnification figure inset in Fig. 2d, we can see that the as-prepared La2S3 microcrystalline is also assembled by a large number of flakes-like structure.
The as-prepared La2S3 microcrystalline is found to be assembled by a large number of flake-like structure.

A number of papers are present in the recent literature on the photodegradation of MCs by TiO2 catalyst[2] and Fenton solvent[3].
All the peaks can be identified to the tetragonal phase of BiOBr corresponding to the dark line (JCPDS card no.03-0993) in the Figure1.
Red curve is XRD pattern of BiOBr, dark line is the standard card and Fig.2 TEM image of BiOBr(a), SEM image of BiOBr(b) and High-Resolution TEM image of BiOBr(c) Table 1.

It is well known that MA processing leads to a continuous decrease in grain size and to an increase of the number of structural defects, local stresses and grain boundaries [9].
The XRD peaks of the lanthanum germanosilicate phase are shifted to lower diffraction angles when compared with the ICDD card of the La9.33Si6O26 phase [10]. 10 20 30 40 50 60 ⊗⊗⊗⊗⊗⊗⊗⊗ ⊗⊗⊗⊗ x x xx ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ ∆∆∆∆ x x x x x οοοο οοοο οοοο οοοο x ♦ ♦♦♦♦-La9.33Si2Ge4O26 x - La2O3; οοοο - SiO2 ∆∆∆∆ - GeO2; ⊗⊗⊗⊗ - La(OH)3 As-blended 150 rpm ♦♦♦ 250 rpm ♦♦♦ ♦ ♦ ♦ ♦ ♦♦ Intensity (a. u.) 2θθθθ (º) ♦ 350 rpm ♦♦ ♦ ♦♦ ♦ ∆∆∆∆ x οοοο ∆∆∆∆οοοο Figure 1 - XRD patterns of the mixture before and after mechanical alloying for 50 h at 150, 250 and 350 rpm.
Vol. 46 (2001), p. 1 [10] JCPDS- International Centre for Diffraction Data, ICDD card nº 49-0443 [11] G.

A small number of flower-like structures compared to the majority oval type structure suggest that secondary nucleation had occurred during the process of growth.
All of the high intensity peaks can be indexed as hexagonal wurtzite structures of ZnO with lattice parameter of a = 3.24982 Å and c = 5.20661 Å (JCPDS Card No. 36-1451) indicating the product is pure.

The structure of the sample pre-sintered at 1100 oC exhibit low crystalline, while at 1350 oC sintering temperature clearly showed the presence of the single-phase cubic structure according to the pattern reference of SmIG, card no: 01-073-1379 [11].
Density value of 6.221 g.cm-3, was calculated for the sintered SmIG sample at 1350 oC, which is in good agreement with the published value [11], according to the formula [12]: (2) where, M = molecular mass of the sample (g/mol), N = Avogadro’s number (6.02214179 x1023 entities/mol) and, a = lattice constant (cm).
Swarthmore., Joint Committee on Powder Diffraction Standards (JCPDS): Powder diffraction data, Card No: 01-073-1379, the National Bureau of Standards,1976

The spectral plots were compared with details obtained from the Joint Committee on Powder (JCPDS) for analytical purposes.
The assignment to a JCPDS card and diffractions of the phases was difficult because the soils contain a significant part of minerals like quartz, clays, kaolinite, and mullite but, all of them contain Si and O [31,32].
Table 1 shows the morphological and structural properties of nanocomposite synthesized with Vertisol-soil (7NC) obtained by the software mentioned before and confirmed with the JCPDS cards.
Nanomaterials, 8 (2018) article number 1012 [23] K.
Lett., 11-1, (2016) Article number 520 [24] Y.

However the price of palladium is too high, which causes a serious pressure for the MLCC production, especially when the number of dielectric layers rapidly increases today [1].
In another aspects, the increasing of dielectric layer number requires diminish of the layer thickness, in turn, the particle size of the powders used for the dielectric ceramic layers in MLCC.
The phase composition of the powder was identified by comparison of interplanar spacings with BaTiO3 perovskite given by the JCPDS cards.

Compared with JCPDS standard cards, the XRD pattern of HA ceramics surface could be indexed to belong to HA single phase, crystals developed in the course of nature in different orientation (fig.2.a).
But on the surface of HA/TCP ceramics, there were some weak IR characteristic absorbed peaks of octacalcium phosphate (OCP) appeared at Wave number (cm -1) b) Fig.4.
Infared spectra of (a) HA ceramics and (b) HA/TCP ceramics immersed in FCS for 7 days 1000 2000 3000 4000 HA-dense OH - P-O Wave number (cm -1) a) 1000 2000 3000 4000 HT-dense P-O OH - OCP 30 31 32 33 34 35 a) HA basement b) HA/TCP basement 2 theta b) a) O O O O O O=OCP 24.0 24.5 25.0 25.5 26.0 26.5 27.0 a) b) a) HA basement b) HA/TCP basement 2 theta O O=OCP Fig.3.