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TF-XRD patterns of the TiO2-coated substrates derived from sol E20 or E50, and subsequently heated at 500°C for 10 min indicated that the peak intensity of anatase (JCPDS card: 21-1272) was increased with increasing number of dip-coating (not shown here).
Table 3 shows the number of platelets adhered on each sample after contact with PRP for 30 min.
Here, the number of Table 3 The number of platelets adhered on each sample after contacted with PRP for 30 mim.
The number of immersions influenced the number of adherent platelets.
The difference in the number of adherent platelets with the number of immersion times was statistically significant.

The value was matched as JCPDS card number for a hexagonal phase wurtzite structure (Space group number 186, Reference code 00-025-1133) [16].
The peak of (002) corresponds to the AlN and the three peaks of (200), (220), and (311) corresponds to the copper substrate verified by JPCD card number 01-089-2838 [17].

Fig.1 shows the standard card for Y2WO6 and the XRD patterns of Y2WO6:Yb3+/Ho3+ prepared with Ho3+ doped and Yb3+/Ho3+ co-doped by solid state reaction and heat-treated at 1200℃.
As shown, all samples were well indexed with the JCPDS file no. 23-1489 (Y2WO6 phase), indicating that the structure of Y2WO6 were not changed with co-doping Yb3+/Ho3+, and the structure of powers also belong to monoclinic system, reflecting the similar reactivity of lanthanide ions [17].
Fig. 1 XRD patterns of Y2WO6: Ho3+/Yb3+ phosphors and JCPDS file no.23-1489 as a reference.
To analyze the UC mechanism, the number of NIR pump photons in the UC emission process can be explained by changing the UC emission intensity as a function of the pump power.
It is well known that the UC intensity(IUC) is proportional to the infrared power n of the excitation power(P): , where n is the absorbed photon numbers per visible photon emitted, A plot of yields a straight line with slop n [4,18].

The results indicated that the basicity, the number of strong base center and pore volume and pore size of Y-Mg-Al-LDO were increased.
Fig 1 XRD patterns of YMgAl HTLcs with Fig 2 XRD patterns of YMgAl-LDO different Y3+molar contents with different Y3+ molar contents As shown in Fig.1, all of the samples show the characteristic diffraction lines typical for Mg-Al-LDH at near 2θ=12 °, 24 °, 35 °, 39 °, 46 °, 61 °, 62 ° (compared with the standard card JCPDS NO.38-0487 ), which has obvious peak shape and thus prove that the samples exhibits a good crystallinity and crystal shape integrity.
The alkali strength is improved and number is markedly increased.
Based on the characterization results, Y3+ doesn’t change hydrotalcite’s layered crystal structure, but other related parameters, i.e. the pore volume, pore diameter, basic strength and the number of strong base center, have increased, which could speed up the diffusion of acetone gas molecules in the mesoporous, provide more catalytic activity center for the catalytic reaction, and further improve the catalytic activity of the catalyst.

Subsequently, the grains were refined and became tiny grains under the action of a large number of edge dislocations in the crystals.
Because BP belongs to the orthorhombic system, the lattice plane indices corresponded to BP (13), (1), (00), (20) and the crystal zone axis is [101], which were consistent with the values reported for JCPDS card No. 73-1358.
This shows that the amorphous phosphorus turned into BP nanocrystals under the action of mechanical milling, and that large numbers of edge dislocations were produced in the crystals due to plastic deformation.
(3) The morphology of the crystal showed that the amorphous phosphorus turned into large size BP nanocrystals under the action of mechanical milling and then, upon being refined, became tiny grains under the action of a large number of edge dislocations.

The XRD patterns of the pyrolysed and oxidized samples were compared with several possible phases carrying out an accurate search in the JCPDS data bank [16].
In fact, the diffraction peak centered on 23º (2-theta) refers to synthetic amorphous SiO2 cristobalite phase (PDF number 39-1425).
However, at very low angles, specifically bellow 8º (2-theta), is observed an intense peak very similar to several MCM-48 silica material types, very well represented by PDF 51-1592 card.
All of them can be associated to synthetic NiO bunsenite (PDF number 47-1039), are absent in pyrolysed sample (as prepared) and emerge already after 1 hour of oxidation, getting more intense s a function of the oxidation time.
[16] JCPDS - Joint Committee on Powder Diffraction Standards/International Center for Diffraction Data, Pennsylvania, Powder Diffraction File 2003.

The sample appeared to be phase pure, and the pattern has been indexed to represent the cubic pyrite (FeS2) phase (JCPDS card No.71-0053).
The interfacial resistances (Rf) of Li/pyrite cells with the electrolytes containing different lithium salts as a function of the cycle number are presented in Table 1.
Fig. 3 shows the varaiation of discharge capacity with cycle number for Li/pyrite batteries with various lithium salts in TEGDME solvent.
A continued decreasing trend in interfacial resistance with cycle number was observed only in the case of LiTFSI system.
Discharge curves of Li/pyrite cells with different lithium salt-based liquid electrolytes, as a function of cycle number (0.1C current density) Fig. 4.

On the one hand, this is because that the number of electrons trapped by defect levels increased with the increase of Dy3+.
According to the XRD peaks and the JCPDS cards, it proved that the main crystal phase can be identified as SrAl2O4 phase.
It’s can be conferred that the number of electrons trapped by defect levels increased with the increase of Dy3+, and those electrons can be released after illuminated so that the afterglow property is improved.

The spherical LiFePO4/C particles consisted of a number of smaller grains.
All of the diffraction peaks, strong, narrow and similar, are indicating the high crystallinity of the two samples and can be well indexed to ordered orthorhombic olivine crystalline structure (JCPDS card no. 40-1499), which is consistent with a previous report [3].
(1) where A is the surface area of the cathode material, n is electron number for each molecule during Li ion insertion, F is the Faraday constant, C is Li ion concentration and σ is the Warburg coefficient.

For each sample, all the peaks can be indexed to the body centred cubic (bcc) structural In2O3 with lattice constant of a = 10.11Å (JCPDS card No.06-0416).
The bottom spectrum diagram refers to the standard bulk In2O3 (JCPDS card No.06-0416).
Interestingly, when the argon flow rate increased to 100 sccm, it is seen that the nanorods completely disappeared and a large number of nanocubes with ~500 nm edge length grew into one another.
It is further observed that a large number of particles are coated on the surface of the nanorod, which is connected with the growth mechanism of In2O3 nanorods.
The transport of the gas flowing depends on the Reynolds number (Re), which determines whether it belongs to the laminar flow conditions (2300) or turbulent conditions (4000).