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And all the peaks can be indexed as a tetragonal phase, approaching the standard values for the powder GdVO4, which is in good agreement with literature data (JCPDS Card No. 72–0277) [14].
Typical peaks of GdVO4, which is in good agreement with literature data (JCPDS Card No. 72–0277) [14], are found in the XRD results of the samples heated 12 h and 24 h at 180˚C with pH 4, which means pure phase aim-productions obtained.
All XRD patterns can be readily indexed to a zirconia-type tetragonal structure with lattice constants comparable to the values given in JCPDS 72–0277 [14].
But a second phase could be detected when the pH rose to 14, and all the peaks of second phase could be indexed to the Gd(OH)3 (JCPDS Card No.38-1042) [14] with hexagonal structure.
A23 (2005), p. 1124 [14] JCPDS—International Center for Diffraction Data, Nos.: 72–0277, 38-1042, (2000)

The spectrophotometer visible was used to observe the absorbance of the samples in the wave number of 540 nm for the DNS test and 520 nm for the Seliwanoff test.
In Table 3, Fe-zeolite was compared with existing JCPDS data from some references.
According to the JCPDS Card No: 5-0490 [14], there were a majority of SiO2 compounds in the form of quartz.
Based on JCPDS Card No: 6-239, the peaks include the mordenite phase and according to JCPDS Card No: 17-0143 [15], it was detected as a clinoptilolite mineral component.
The comparison of Fe-zeolite XRD pattern with JCPDS data Compounds 2θ References JCPDS Fe-Zeolite Quarts (JCPDS Card No: 5-0490) 26.68 26.65 [14] 20.90 20.81 50.08 50.10 Mordenite (JCPDS Card No: 6-239) 22.25 22.31 [15] 25.61 25.65 27.79 27.75 Clinoptilolites (JCPDS Card No: 17-0143) 23.84 23.62 [15] Furthermore, Match 3 reported that this Fe-zeolite catalyst had a degree of crystallinity of around 27.79% while the amorphous phase was 72.21%.

It is speculated the number of H + ions adsorbed into the thin film increased with increasing the deposition time and H + ions are removed from the thin film as the H2 gas in the drying process.
TiO2 Anatase type JCPDS Card TiO2 particle (P-25) ITO glass TiO2 thin film on ITO glass TiO2 thin film + Ruthenium complex on ITO glass TiO2 Rutile type JCPDS Card Intensity / a.u. 90 80 70 60 50 40 30 20 10 2θ / deg.
TiO2 particle (P-25) TiO2 Anatase type JCPDS Card TiO2 thin film on ITO glass after thermal annealing at 450 ͠ TiO2 Rutile type JCPDS Card TiO2 thin film on ITO glass after thermal annealing at 500 ͠ TiO2 thin film on ITO glass after thermal annealing at 550 ͠ Fig.4.

All of the calcined samples were characterized by X-ray diffraction by using of D5005 Siemens equipment operating with K-alpha Cu radiation and the phase identification was made by consult in JCPDS data bank [16].
By observing the X-ray diffraction patterns for calcined samples at 100 and 500 ºC for 4 hours in the Fig. 2, it is possible to observe the predominant phase peaks match with the peak of two R-3m rhombohedral reference phases of JCPDS data bank with card numbers 89-461 and 89-5434 (§).
In no co-substituted sample calcined at 100 ºC (Fig 2.a) was found a little peak associated to the nitratine NaNO3 phase (o), available on JCPDS card number 89-2828.
In both samples calcined at 500 ºC, the rhombohedral structures undergo phase decomposition and originate the periclase MgO phase (JCPDS card 45-946), which are marked with x symbol.
[16] JCPDS - Joint Committee on Powder Diffraction Standards/International Center for Diffraction Data, Pennsylvania, Powder Diffraction File 2003

However, during calcination large number of ionized oxygen vacancies is created.
At 800 oC with 0 to 4 mol % of Mn, Fig. 1 (a-c), a single phase of BaTiO3 with tetragonal structure was obtained corresponding to the JCPDS File Card No. 83-1880 [9].
At 900 oC with 2 and 4 mol % of Mn, Fig. 1 (e,f), a single phase of Ba(Mn0.33Ti0.67)O2.84 with hexagonal structure at 2θ = 41.989 was obtained corresponding to the JCPDS Card File No. 15-0239 [8].
Powder Diffraction File, Card No. 150239 Swarthmore, PA [9] Joint Committee on Powder Diffraction Standards.
Powder Diffraction File, Card No. 831880 Swarthmore, PA

The main peaks of the present samples compared with the standard JCPDS cards.
Sample JCPDS file no.
X-Ray Diffraction pattern of sample A and sample B compared with the standard JCPDS cards of goethite (C) and magnetite/maghemite (D).
However, in Sample B that was prepared after about 1-2 days, particle size distribution consists of two fractions: a large number of small magnetic particles with average diameter 140.7 nm and a small part number of large aggregates with average diameter 669,7 nm.
Acknowledgment This research received financial support from grant number 178/SP2H/LT/DPRM/2019, by the Department of Ministry of Research, Technology, and Higher Education of Republic Indonesia, through the Institute for Research and Community Services of Lambung Mangkurat University with contract number: 123.5/UN8.2/PP/2019.

Figure 2 : TEM pictures of Ni(OH)2 and NiO particles Another interesting parameter is the relationship between the initial and final particle numbers.
We both calculate this average number of Ni atoms in a Ni(OH)2 platelet and also in a NiO sphere.
The position of the main peak of cobalt hydroxide is extracted from the JCPDS cards number 741057.
We obtain the best agreement of our spectrum with the nickel cobalt oxide Ni1.71 Co1.29O4 (JCPDS card 401191).
This spinel structure is very close to that of cobalt oxide Co3O4 (JCPDS 741656) which is the result of the thermal transformation of the pure cobalt hydroxide [15] Co(OH)2 (JCPDS card 741057).

The XRD patterns were phase identified using the JCPDS data bank [23] and the anatase and rutile structural models were taken from ICSD data bank [24].
There is no evidence of rutile phase for any composition up to 600 ºC and the diffraction peaks observed correspond to the crystalline planes (101), (004), (200), (105), (211), (204) and (106) for anatase phase available on JCPDS card number 71-11166 [23].
For unmodified samples, the anatase-to-rutile phase transition can be verified at 700 ºC through the peaks associated to the crystalline planes (110), (011), and (121), according the rutile phase available on diffraction pattern data bank in JCPDS card number 73-1232 [23].
The Rietveld refinement was carried out starting from anatase and rutile structural models available on crystal structures data bank in ICSD card numbers 82084 and 53997, for anatase and rutile structures, respectively [24].
[23] JCPDS - Joint Committee on Powder Diffraction Standards/International Center for Diffraction Data, Pennsylvania, Powder Diffraction File, 2003

A number of methods have been developed to synthesize W nanocrystals, including mechanical milling [6], laser irradiation [7], electron beam-induced deposition [8] and solvothermal methods [9].
The as-obtained product can be indexed to monoclinic WO3, according to JCPDS card no. 43-1035.
The major phase of the product obtained at 900 oC for 2 h are monoclinic WO3 (JCPDS card No. 43-1035), as shown as Fig. 3a.
The samples obtained at 900 oC for 6 h and at 1000 oC for 2 h (Figs. 3b–c) mainly consist of the WO2 phase (JCPDS card no. 32-1393).
With a long reaction time to 4 h at 1000 oC, a large fraction of cubic W phase (JCPDS card no. 04-0806) is obtained, as shown in Fig. 3d, besides a small amount of the WO2 phase.

Fig. 1a depicts the formation of corundum – the primary crystalline phase of alumina (Al2O3) (JCPDS card no. 75-0783), which is known to be most stable phase of alumina at temperatures above 1290°C [17].
Fig. 1b shows the formation of calcium hydroxyapatite (HAp) as a single phase, which is confirmed by the presence of the main diffraction peaks of hydroxyapatite [Ca10(PO4)6(OH)2] identified based on JCPDS card no. 89-6437.
In this figure, note the formation of α-Al2O3 crystalline rhombohedral phase, in the form of the mineral corundum (JCPDS card no. 10-0173).
The diffractograms corresponding to the composites containing HAp (A20 and A30) show the presence of α-Al2O3 and hydroxyapatite [Ca10(PO4)6(OH)2 - HAp] (JCPDS card no. 86-0740).
This introduction led to an increase in the number of grain boundaries (Fig. 3), thus increasing the barrier mechanism against applied stress and significantly reducing the intensity of this stress over the applied area by dividing it into a series of lower stresses.