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12 pages, 6711 KiB  
Article
Crystal Structure and Microwave Dielectric Characteristics of Novel Ba(Eu1/5Sm1/5Nd1/5Pr1/5La1/5)2Ti4O12 High-Entropy Ceramic
by Qing Wan, Zeping Li, Huifeng Wang, Gang Xiong and Geng Wang
Crystals 2024, 14(9), 754; https://doi.org/10.3390/cryst14090754 - 25 Aug 2024
Viewed by 542
Abstract
High-permittivity Ba(Eu1/5Sm1/5Nd1/5Pr1/5La1/5)2Ti4O12 (BESNPLT) high-entropy ceramics (HECs) were synthesized via a solid-state route. The microstructure, sintering behavior, phase structure, vibration modes, and microwave dielectric characteristics of the BESNPLT HECs [...] Read more.
High-permittivity Ba(Eu1/5Sm1/5Nd1/5Pr1/5La1/5)2Ti4O12 (BESNPLT) high-entropy ceramics (HECs) were synthesized via a solid-state route. The microstructure, sintering behavior, phase structure, vibration modes, and microwave dielectric characteristics of the BESNPLT HECs were thoroughly investigated. The phase structure of the BESNPLT HECs was confirmed to be a single-phase orthorhombic tungsten-bronze-type structure of Pnma space group. Permittivity (εr) was primarily influenced by polarizability and relative density. The quality factor (Q×f) exhibited a significant correlation with packing fraction, whereas the temperature coefficient (TCF) of the BESNPLT HECs closely depended on the tolerance factor and bond valence of B-site. The BESNPLT HECs sintered at 1400 °C, demonstrating high relative density (>97%) and optimum microwave dielectric characteristics with TCF = +38.9 ppm/°C, Q×f = 8069 GHz (@6.1 GHz), and εr = 87.26. This study indicates that high-entropy strategy was an efficient route in modifying the dielectric characteristics of tungsten-bronze-type microwave ceramics. Full article
(This article belongs to the Special Issue Crystal Structure and Dielectric Properties of Ceramics)
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Figure 1
<p>XRD patterns of BESNPLT HECs sintered at 1350–1500 °C.</p>
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<p>(<b>a</b>) Rietveld refinement plots of BESNPLT HECs. (<b>b</b>) Structural diagram of BESNPLT HECs.</p>
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<p>Raman spectra of BESNPLT HECs sintered at varying temperatures.</p>
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<p><span class="html-italic">ρ<sub>re</sub></span> and <span class="html-italic">ρ<sub>bu</sub></span> of BESNPLT HECs sintered at 1350–1500 °C.</p>
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<p>SEM morphology of BESNPLT HECs sintered at (<b>a</b>) 1350 °C; (<b>b</b>) 1400 °C; (<b>c</b>) 1450 °C; (<b>d</b>) 1500 °C.</p>
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<p>EDS mapping of BESNPLT HECs.</p>
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<p>(<b>a</b>) <span class="html-italic">ε<sub>r</sub></span> and <span class="html-italic">ρ<sub>re</sub></span> of BESNPLT HECs; (<b>b</b>) <span class="html-italic">ε<sub>cor</sub></span> and <span class="html-italic">α<sub>the</sub>/<span class="html-italic">V<sub>m</sub></span></span> of BESNPLT HECs.</p>
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<p>(<b>a</b>) <span class="html-italic">Q×f</span> and <span class="html-italic">ρ<sub>re</sub></span> of BESNPLT HECs; (<b>b</b>) <span class="html-italic">Q×f</span> and packing fraction of BESNPLT HECs.</p>
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<p>(<b>a</b>) TCF and B-site bond valence of BESNPLT HECs; (<b>b</b>) BaLa<sub>2</sub>Ti<sub>4</sub>O<sub>12</sub> (BLT) [<a href="#B36-crystals-14-00754" class="html-bibr">36</a>], BaPr<sub>2</sub>Ti<sub>4</sub>O<sub>12</sub> (BPT) [<a href="#B56-crystals-14-00754" class="html-bibr">56</a>], BaNd<sub>2</sub>Ti<sub>4</sub>O<sub>12</sub> (BNT) [<a href="#B57-crystals-14-00754" class="html-bibr">57</a>], BaSm<sub>2</sub>Ti<sub>4</sub>O<sub>12</sub> (BST) [<a href="#B58-crystals-14-00754" class="html-bibr">58</a>], and BESNPLT ceramics.</p>
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12 pages, 3362 KiB  
Article
Zero-Temperature Coefficient of Resonant Frequency in [(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02-Ca0.6(La0.9Y0.1)0.2667TiO3 Ultra-Low-Loss Composite Dielectrics
by Yuan-Bin Chen and Jie Peng
Ceramics 2024, 7(2), 466-477; https://doi.org/10.3390/ceramics7020030 - 26 Mar 2024
Viewed by 1261
Abstract
Investigating the microwave dielectric properties of ceramics prepared through the conventional solid-state route, such as x[(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02-(1−x)Ca0.6(La0.9Y0.1)0.2667TiO3, reveals notable characteristics. [(Mg0.6 [...] Read more.
Investigating the microwave dielectric properties of ceramics prepared through the conventional solid-state route, such as x[(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02-(1−x)Ca0.6(La0.9Y0.1)0.2667TiO3, reveals notable characteristics. [(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02 shows a permittivity (εr) of approximately 20, a high quality factor (Q × f) ranging between 250,000 and 560,000 GHz, and a temperature coefficient of resonant frequency (τf) of approximately −65 ppm/°C. To enhance the temperature stability, Ca0.6(La0.9Y0.1)0.2667TiO3 featuring a τf value of +374 ppm/°C was incorporated into the [(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02 composition. τf demonstrated an increase with rising Ca0.6(La0.9Y0.1)0.2667TiO3 content, reaching zero at x = 0.95. A ceramic composition of 0.95[(Mg0.6Zn0.4)0.95Co0.05]1.02TiO3.02-0.05Ca0.6(La0.9Y0.1)0.2667TiO3, incorporating 3wt.% BaCu(B2O5) as sintering aids, exhibited outstanding microwave dielectric properties: εr~22.5, Q × f~195,000 (at 9 GHz), and τf~0.1ppm/°C, with a sintering temperature at 950 °C. This material is proposed as a prospective candidate for 6G band components and GPS antennas. Full article
(This article belongs to the Special Issue Advances in Electronic Ceramics)
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<p>X-ray diffraction patterns of 0.95MZCT-0.05CLYT ceramics doped with 3wt.% BCB and sintered at various temperatures for 4 h: (<b>a</b>) 900 °C, (<b>b</b>) 925 °C, (<b>c</b>) 950 °C, (<b>d</b>) 975 °C, and (<b>e</b>) 1000 °C (♣: MZCT; ★: CLYT).</p>
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<p>SEM micrographs of 0.95MZCT-0.05CLYT ceramics doped with 3wt.% BCB and sintered at (<b>a</b>) 900, (<b>b</b>) 925, (<b>c</b>) 950, (<b>d</b>) 975, and (<b>e</b>) 1000 °C.</p>
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<p>SEM micrographs of 0.95MZCT-0.05CLYT ceramics doped with 3wt.% BCB and sintered at (<b>a</b>) 900, (<b>b</b>) 925, (<b>c</b>) 950, (<b>d</b>) 975, and (<b>e</b>) 1000 °C.</p>
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<p>The marks of SEM for the 0.95MZCT-0.05CLYT ceramics doped with 3wt.% BCB and sintered at 950 °C.</p>
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<p>(<b>a</b>) Bulk density, (<b>b</b>) relative density, and (<b>c</b>) porosity of xMZCT-(1-x)CLYT ceramics with 3wt.% BCB as a function of the sintering temperature.</p>
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<p>(<b>a</b>) Bulk density, (<b>b</b>) relative density, and (<b>c</b>) porosity of xMZCT-(1-x)CLYT ceramics with 3wt.% BCB as a function of the sintering temperature.</p>
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<p>Permittivity curves of xMZCT-(1−x)CLYT ceramics doped with 3wt.% BCB at different sintering temperatures for 4 h.</p>
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<p>Q × f values of xMZCT-(1−x)CLYT ceramics doped with 3wt.% BCB as a function of the sintering temperature.</p>
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<p>τ<sub>f</sub> values of the xMZCT-(1−x)CLYT ceramic system with 3 wt.% BCB sintered at different temperatures for 4 h.</p>
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20 pages, 3666 KiB  
Article
Trace Elements in Pernik Sub-Bituminous Coals and Their Combustion Products Derived from the Republika Thermal Power Station, Bulgaria
by Mariana G. Yossifova, Greta M. Eskenazy, Stanislav V. Vassilev and Dimitrina A. Dimitrova
Minerals 2024, 14(3), 313; https://doi.org/10.3390/min14030313 - 16 Mar 2024
Viewed by 1290
Abstract
The contents of 49 trace elements in sub-bituminous Pernik coals and their waste products from preparation and combustion processes were investigated. The studied coals have trace element contents higher than the respective Clarke values for brown coals and some of them may pose [...] Read more.
The contents of 49 trace elements in sub-bituminous Pernik coals and their waste products from preparation and combustion processes were investigated. The studied coals have trace element contents higher than the respective Clarke values for brown coals and some of them may pose environmental concerns. The elements Li, Rb, Cs, Ba, Sc, Y, La, Ce, Nd, Sm, Eu, Er, Ga, Zr, Sn, V, Nb, Ta, W, F, Cu, Zn, In, Pb, Cr, Co, Ni, and Th in the feed coals have concentrations that exceed twice the Clarke values. Most element contents in bottom ash are enriched compared with those in feed coal. Some of the volatile elements are equal or significantly depleted including Sn, Mo, Sb, F, Bi, Cd, Ge, and Pb. Fly ash has higher contents of Ga, Zr, Hf, Sn, V, Nb, Mo, and F in comparison with bottom ash. Most elements have a significant positive correlation with ash yield, indicating their inorganic association. The mixed wastes (coal slurry, bottom ash, and fly ash) in the disposal pond are slightly depleted of most of the elements studied with the exclusion of Cl, Ba, and Br. The Pernik coals and their waste products are unpromising for the extraction of REY due to their low element contents. Full article
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<p>(<b>A</b>) Map of Bulgaria and (<b>B</b>) location of the Pernik coal preparation plant, the Republika thermoelectric power station, and the Pernik coal mines.</p>
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<p>SEM back-scattered images of (<b>A</b>) porous spheroidal char covered with Fe oxide film (fly ash, fraction 1–0.5 mm); (<b>B</b>) fusinoid char covered with aluminosilicate film (fly ash, fraction 1–0.5 mm).</p>
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<p>Concentration coefficients (CCs) [<a href="#B32-minerals-14-00313" class="html-bibr">32</a>]: trace element contents in the Pernik coals and waste products/trace element world averages for brown coals by Ketris and Yudovich [<a href="#B1-minerals-14-00313" class="html-bibr">1</a>].</p>
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<p>Distribution of the elements in the bottom ash size fractions. (<b>A</b>) The first group is represented via Yb. (<b>B</b>) The second group is represented via La. (<b>C</b>) The third group is represented via Ge. (<b>D</b>) The fourth group is represented via F.</p>
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<p>Normalized REE patterns of the Pernik coals and waste products to (<b>A</b>) chondrite [<a href="#B33-minerals-14-00313" class="html-bibr">33</a>] and (<b>B</b>) shales [<a href="#B73-minerals-14-00313" class="html-bibr">73</a>].</p>
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<p>Evaluation of REY in the studied samples using the outlook coefficient (Coutl), established by Seredin and Dai [<a href="#B2-minerals-14-00313" class="html-bibr">2</a>], in a plot as in Dai et al. [<a href="#B80-minerals-14-00313" class="html-bibr">80</a>].</p>
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16 pages, 2394 KiB  
Review
Production of Medical Radionuclides in the Center for Radiopharmaceutical Tumor Research—A Status Report
by Martin Kreller, Santiago Andrés Brühlmann, Torsten Knieß, Klaus Kopka and Martin Walther
Instruments 2024, 8(1), 10; https://doi.org/10.3390/instruments8010010 - 7 Feb 2024
Viewed by 1690
Abstract
A new Center for Radiopharmaceutical Cancer Research was established at the Helmholtz-Zentrum Dresden-Rossendorf in 2017 to centralize radionuclide and radiopharmaceutical production, as well as enable chemical and biochemical research. Routine production of several radionuclides was put into operation in recent years. We report [...] Read more.
A new Center for Radiopharmaceutical Cancer Research was established at the Helmholtz-Zentrum Dresden-Rossendorf in 2017 to centralize radionuclide and radiopharmaceutical production, as well as enable chemical and biochemical research. Routine production of several radionuclides was put into operation in recent years. We report on the production methods of radiopharmaceutical radionuclides, in particular 11C, 18F, and radio metals like 61Cu, 64Cu, 67Cu, 67Ga, 131Ba, and 133La that are used regularly. In the discussion, we report typical irradiation parameters and achieved saturation yields. Full article
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<p>The TR-Flex installed at the HZDR with target selector 1B at the front.</p>
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<p>Produced radiopharmaceuticals from 2018 to 2022.</p>
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<p>The solid target holder including the energy degrader (right side after irradiation with about 5000 µAh) is shown in the upper part of the picture. The energy degrader is integrated into the cooling circuit of the solid target holder. In the lower part, a scheme of the energy degrader including the cooling channels is shown on the left side. The temperature of the energy degrader is simulated to be below 400 °C with ion currents up to 80 µA using the COMSOL 5.5 software.</p>
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<p>Electroplated <sup>64</sup>Ni target on a gold backing used for routine <sup>64</sup>Cu production.</p>
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<p>Radiochemical separation methods used for <sup>61</sup>Cu purification from <sup>62</sup>Ni targets [<a href="#B8-instruments-08-00010" class="html-bibr">8</a>].</p>
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<p>Cross-section of the <sup>70</sup>Zn(p,α)<sup>67</sup>Cu. Dotted lines: the energy degraded for two different targets’ thicknesses [<a href="#B12-instruments-08-00010" class="html-bibr">12</a>].</p>
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<p>Gamma spectroscopy of the raw target solution (<b>a</b>) and [<sup>67</sup>Cu]CuCl<sub>2</sub> product fraction (<b>b</b>) [<a href="#B21-instruments-08-00010" class="html-bibr">21</a>].</p>
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<p>Radiochemical separation method scheme for <sup>67</sup>Ga purification.</p>
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<p>Cross-section of relevant nuclear reactions leading to lanthanum radionuclides weighted for the [<sup>134</sup>Ba]BaCO<sub>3</sub>-enriched target [<a href="#B35-instruments-08-00010" class="html-bibr">35</a>]. The energy windows studied are shown with the dotted lines.</p>
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<p>Elution profile of the used 2 mL bDGA cartridge for the <sup>133</sup>La purification [<a href="#B28-instruments-08-00010" class="html-bibr">28</a>].</p>
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14 pages, 9067 KiB  
Article
Barium Lanthanum Oxide Nanosheets in Photocatalytic and Forensic Applications: One-Pot Synthesis and Characterization
by Sanjay S. Majani, Meghana, Sowmyashree S H, Sowjanyashree J, Sahaja Umesh, Chandan Shivamallu, Muzaffar Iqbal, Raghavendra G. Amachawadi, Venkatachalaiah K N and Shiva Prasad Kollur
Molecules 2023, 28(20), 7228; https://doi.org/10.3390/molecules28207228 - 23 Oct 2023
Cited by 2 | Viewed by 1333
Abstract
The present work elucidates the fabrication of Barium Lanthanum Oxide nanosheets (BaLa2O4 NSs) via a simple one-pot precipitation method. The acquired results show an orthorhombic crystal system with an average crystallite size of 27 nm. The morphological studies revealed irregular-shaped [...] Read more.
The present work elucidates the fabrication of Barium Lanthanum Oxide nanosheets (BaLa2O4 NSs) via a simple one-pot precipitation method. The acquired results show an orthorhombic crystal system with an average crystallite size of 27 nm. The morphological studies revealed irregular-shaped sheets stacked together in a layered structure, with the confirmation of the precursor elements. The diffused reflectance studies revealed a strong absorption between 200 nm and 350 nm, from which the band-gap energy was evaluated to be 4.03 eV. Furthermore, the fluorescence spectrum was recorded for the prepared samples; the excitation spectrum shows a strong peak at 397 nm, attributed to the 4F7/24G11/2 transition, while the emission shows two prominent peaks at 420 nm (4G7/24F7/2) and 440 nm (4G5/24F7/2). The acquired emission results were utilized to confirm the color emission using a chromaticity plot, which found the coordinates to be at (0.1529 0.1040), and the calculated temperature was 3171 K. The as-prepared nanosheets were utilized in detecting latent fingerprints (LFPs) on various non-porous surfaces. The powder-dusting method was used to develop latent fingerprints on various non-porous surfaces, which resulted in detecting all the three ridge patterns. Furthermore, the as-synthesized nanosheets were used to degrade methyl red (MR) dye, the results of which show more than 60% degradation at the 70th minute. It was also found that there was no further degradation after 70 min. All the acquired results suggest the clear potential of the prepared BaLa2O4 NSs for use in advanced forensic and photocatalytic applications. Full article
(This article belongs to the Special Issue Synthesis and Application of Nanoparticles and Nanocomposites)
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Graphical abstract
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<p>XRD profile of prepared BaLa<sub>2</sub>O<sub>4</sub> NSs assigned with hkl values from mp-752656.</p>
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<p>FESEM micrographs with different resolutions ((<b>a</b>) 1 µm, and (<b>b</b>–<b>d</b>) 100 nm) of the as-prepared BaLa<sub>2</sub>O<sub>4</sub> NSs.</p>
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<p>EDAX spectrum showing high purity of precursor elements.</p>
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<p>Mapping of precursor elements over a selected area using EDAX analysis.</p>
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<p>DR spectrum (<b>a</b>) and band-gap calculation (<b>b</b>) of the prepared BaLa<sub>2</sub>O<sub>4</sub> NSs.</p>
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<p>(<b>a</b>) Excitation spectrum at λ<sub>emi</sub> = 440 nm, and (<b>b</b>) emission spectrum at λ<sub>exi</sub> = 397 nm of the prepared BaLa<sub>2</sub>O<sub>4</sub> NSs.</p>
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<p>CIE (<b>a</b>) and CCT (<b>b</b>) plot using emission at λ<sub>exi</sub> = 397 nm of the prepared BaLa<sub>2</sub>O<sub>4</sub> NSs. <span class="html-fig-inline" id="molecules-28-07228-i001"><img alt="Molecules 28 07228 i001" src="/molecules/molecules-28-07228/article_deploy/html/images/molecules-28-07228-i001.png"/></span> represents the point of maximum emission.</p>
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<p>Latent fingerprints developed using powder dusting over glass (<b>A</b>), aluminium (<b>B</b>), and stainless steel (<b>C</b>). The detection was observed at 2× magnification of the captured images.</p>
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<p>Photocatalytic performance of BaLa<sub>2</sub>O<sub>4</sub> NSs against MR dye. (<b>a</b>) Absorption spectrum of as-prepared photocatalyst; (<b>b</b>) graph representing the degradation of MR dye at various concentrations.</p>
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<p>Flowchart representing the one-pot synthesis of BaLa<sub>2</sub>O<sub>4</sub> NSs.</p>
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23 pages, 13693 KiB  
Article
Superconducting and Mechanical Properties of the Tl0.8Hg0.2Ba2Ca2Cu3O9−δ Superconductor Phase Substituted by Lanthanum and Samarium Fluorides
by Rola F. Khattar, Mohammed Anas, Ramadan Awad and Khulud Habanjar
Condens. Matter 2023, 8(4), 87; https://doi.org/10.3390/condmat8040087 - 7 Oct 2023
Viewed by 1261
Abstract
This study investigated the impact of samarium and lanthanum fluorides (SmF3 and LaF3) on the physical and mechanical properties of Tl0.8Hg0.2Ba2Ca2−xRxCu3O9−δ−yFy superconducting phases (specifically [...] Read more.
This study investigated the impact of samarium and lanthanum fluorides (SmF3 and LaF3) on the physical and mechanical properties of Tl0.8Hg0.2Ba2Ca2−xRxCu3O9−δ−yFy superconducting phases (specifically the (Tl, Hg)-1223 phase), where R = Sm and La, with 0.00 x 0.10. The superconducting samples were synthesized using the solid-state reaction method. X-ray diffraction (XRD) verified the formation of the (Tl, Hg)-1223 phase without altering its tetragonal structure. Scanning electron micrographs (SEM) reveal the improvement of the grain size and inter-grain connectivity as Sm and La contents increased up to x=0.025. The electrical properties of (Tl, Hg)-1223 were studied using I-V and electrical resistivity measurements. Improved superconducting transition temperature (Tc) and transport critical current density (Jc) were observed up to x=0.025, beyond which they decreased substantially. Vickers microhardness (Hv) measurements were performed at room temperature to investigate their mechanical performance with various applied loads (0.499.80 N) and times (1090 s). For both substitutions, the mechanical properties were enhanced up to an optimal value at x=0.025. All samples exhibited normal indentation size effect (ISE) behavior. The proportional sample resistance (PSR) model best explained Hv values among five theoretical models. Dislocation creep was the primary creep mechanism in the samples, according to indentation creep studies. Full article
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<p>Typical XRD patterns and the Rietveld refinements of the XRD spectra for Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> superconductor samples, where R = Sm and La.</p>
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<p>Variation of volume fractions (V %) versus SmF<sub>3</sub> and LaF<sub>3</sub> contents of the (Tl, Hg)-1223 phase and the (Tl, Hg)-1212 impurity phase with all other impurities.</p>
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<p>The variation of lattice parameters <span class="html-italic">a</span> and <span class="html-italic">c</span> for Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> as a function of the substitution content <span class="html-italic">x</span>, where (<b>a</b>) R = Sm and (<b>b</b>) R = La.</p>
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<p>Micrographs of (<b>a</b>) Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2</sub>Cu<sub>3</sub>O<sub>9−δ</sub>, (<b>b</b>) Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>1.975</sub>Sm<sub>0.025</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub>, (<b>c</b>) Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>1.9</sub>Sm<sub>0.1</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub>, (<b>d</b>) Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>1.975</sub>La<sub>0.025</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y,</sub> and (<b>e</b>) Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>1.9</sub>La<sub>0.1</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub>.</p>
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<p>Variation of resistivity versus temperature plots for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> phase, with <math display="inline"><semantics> <mrow> <mn>0.00</mn> <mo> </mo> <mo>≤</mo> <mo> </mo> <mi>x</mi> <mo> </mo> <mo>≤</mo> <mo> </mo> <mn>0.10</mn> </mrow> </semantics></math>, where R = Sm and La.</p>
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<p>The electric field variation as a function of the critical current density for Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> superconducting samples, with <math display="inline"><semantics> <mrow> <mn>0.00</mn> <mo> </mo> <mo>≤</mo> <mo> </mo> <mi>x</mi> <mo> </mo> <mo>≤</mo> <mo> </mo> <mn>0.10</mn> </mrow> </semantics></math>, where R = Sm and La. The inset represents the logarithmic plots of (E) versus (J).</p>
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<p>Variations of <span class="html-italic">T<sub>c</sub></span> and <span class="html-italic">J<sub>c</sub></span> versus <span class="html-italic">x</span> for the Tl<sub>0.8-x</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> superconducting phase, with <math display="inline"><semantics> <mrow> <mn>0.00</mn> <mo> </mo> <mo>≤</mo> <mo> </mo> <mi>x</mi> <mo> </mo> <mo>≤</mo> <mo> </mo> <mn>0.10</mn> </mrow> </semantics></math>, where R = Sm and La.</p>
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<p>The variation of <span class="html-italic">H<sub>V</sub></span> as a function of the applied indentation test loads <span class="html-italic">F</span> of Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<span class="html-italic"><sub>x</sub></span>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub>; (<b>a</b>) R = Sm (<b>b</b>) R = La at a dwell time of 20 s.</p>
Full article ">Figure 9
<p><math display="inline"><semantics> <mrow> <mi>l</mi> <mi>n</mi> <mi>F</mi> </mrow> </semantics></math> versus <math display="inline"><semantics> <mrow> <mi>l</mi> <mi>n</mi> <mi>d</mi> </mrow> </semantics></math> for the (<b>a</b>) Sm-substituted samples and (<b>b</b>) La-substituted samples at a dwell time of 20 s.</p>
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<p>Applied loads F versus the square of the impression length for the superconducting samples with (<b>a</b>) Sm substitution and (<b>b</b>) La substitution.</p>
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<p>Variation of F<sup>0.5</sup> against d for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<span class="html-italic"><sub>x</sub></span>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase at a dwell time of 20 s; (<b>a</b>) R = Sm (<b>b</b>) R = La.</p>
Full article ">Figure 12
<p><span class="html-italic">F/d</span> versus <span class="html-italic">d</span> for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<span class="html-italic"><sub>x</sub></span>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase at a dwell time of 20 s; (<b>a</b>) R = Sm (<b>b</b>) R = La.</p>
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<p>F versus d for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<span class="html-italic"><sub>x</sub></span>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase at a dwell time of 20 s; (<b>a</b>) R = Sm (<b>b</b>) R = La.</p>
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<p>Variations of the measured <span class="html-italic">H<sub>V</sub></span> and estimated <span class="html-italic">H<sub>V</sub></span> using various models with the applied load <span class="html-italic">F</span> of the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>Sm<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> phase, with (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.00</mn> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.025</mn> </mrow> </semantics></math>, (<b>c</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.05</mn> </mrow> </semantics></math>, (<b>d</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.075</mn> </mrow> </semantics></math>, and (<b>e</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.10</mn> </mrow> </semantics></math>.</p>
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<p>Variations of the measured <span class="html-italic">H<sub>V</sub></span> and estimated <span class="html-italic">H<sub>V</sub></span> using various models with the applied load <span class="html-italic">F</span> of the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>La<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> phase, with (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.00</mn> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.025</mn> </mrow> </semantics></math>, (<b>c</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.05</mn> </mrow> </semantics></math>, (<b>d</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.075</mn> </mrow> </semantics></math>, and (<b>e</b>) <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>0.10</mn> </mrow> </semantics></math>.</p>
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<p>Variation of the mechanical parameters <span class="html-italic">E</span>, <span class="html-italic">Y</span>, and <span class="html-italic">K</span> for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>R<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> phase with respect to <span class="html-italic">x</span> for (<b>a</b>) R = Sm (<b>b</b>) R = La.</p>
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<p>Variation of <span class="html-italic">H<sub>V</sub></span> versus time at applied loads of (<b>a</b>) <math display="inline"><semantics> <mrow> <mn>2.94</mn> <mo> </mo> </mrow> </semantics></math>N, (<b>b</b>) <math display="inline"><semantics> <mrow> <mn>4.9</mn> </mrow> </semantics></math> N, and (<b>c</b>) <math display="inline"><semantics> <mrow> <mn>9.8</mn> </mrow> </semantics></math> N for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>Sm<sub>x</sub>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase.</p>
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<p>Variation of <span class="html-italic">H<sub>V</sub></span> versus time at applied loads of (<b>a</b>) <math display="inline"><semantics> <mrow> <mn>2.94</mn> </mrow> </semantics></math> N, (<b>b</b>) <math display="inline"><semantics> <mrow> <mn>4.9</mn> <mo> </mo> </mrow> </semantics></math>N, and (<b>c</b>) <math display="inline"><semantics> <mrow> <mn>9.8</mn> </mrow> </semantics></math> N for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>La<sub>x</sub>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase.</p>
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<p>Variation of <span class="html-italic">ln H<sub>V</sub></span> versus <span class="html-italic">ln t</span> at applied loads of (<b>a</b>)<math display="inline"><semantics> <mrow> <mn>2.94</mn> </mrow> </semantics></math> N, (<b>b</b>) <math display="inline"><semantics> <mrow> <mn>4.9</mn> </mrow> </semantics></math> N, and (<b>c</b>) <math display="inline"><semantics> <mrow> <mn>9.8</mn> </mrow> </semantics></math> N for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>Sm<sub>x</sub>Cu<sub>3</sub>O<sub>9−δ−y</sub>F<sub>y</sub> phase.</p>
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<p>Variation of <span class="html-italic">ln H<sub>V</sub></span> versus <span class="html-italic">ln t</span> at applied loads of (<b>a</b>) <math display="inline"><semantics> <mrow> <mn>2.94</mn> </mrow> </semantics></math> N, (<b>b</b>) <math display="inline"><semantics> <mrow> <mn>4.9</mn> </mrow> </semantics></math> N, and (<b>c</b>) <math display="inline"><semantics> <mrow> <mn>9.8</mn> </mrow> </semantics></math> N for the Tl<sub>0.8</sub>Hg<sub>0.2</sub>Ba<sub>2</sub>Ca<sub>2−x</sub>La<sub>x</sub>Cu<sub>3</sub>O<sub>9−<span class="html-italic">δ</span>−y</sub>F<sub>y</sub> phase.</p>
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14 pages, 14453 KiB  
Article
Synthesis, Microstructure, and Electrical Conductivity of Eutectic Composites in MF2–RF3 (M = Ca, Sr, Ba; R = La–Nd) Systems
by Irina I. Buchinskaya, Natalia A. Arkharova, Anna G. Ivanova, Nikolay I. Sorokin and Denis N. Karimov
J. Compos. Sci. 2023, 7(8), 330; https://doi.org/10.3390/jcs7080330 - 15 Aug 2023
Cited by 1 | Viewed by 1180
Abstract
Multiphase fluoride polycrystalline eutectics pRF3 × qMF2 forming in the MF2–RF3 (M = Ca, Sr, Ba; R = La–Nd) binary systems were synthesized by the directional crystallization technique from a melt. The phase composition, morphology, and [...] Read more.
Multiphase fluoride polycrystalline eutectics pRF3 × qMF2 forming in the MF2–RF3 (M = Ca, Sr, Ba; R = La–Nd) binary systems were synthesized by the directional crystallization technique from a melt. The phase composition, morphology, and temperature dependences of fluorine ionic conductivity in fabricated composites were studied in detail. The pRF3 × qMF2 (p and q are the mole percentages of components) eutectic composites consist of both extremely saturated fluorite-type structure M1−xRxF2+x solid solutions and the tysonite-type R1−yMyF3−y ones. Microsized growth blocks with a fine lamellar structure are typical for synthesized composites. The thinnest (from 3 μm) and longest lamellae are observed in the 68LaF3 × 32BaF2 composition. The ionic conductivity values of pRF3 × qMF2 composites are determined by the phase composition, practically do not depend on their morphological features, and reach 10−3–10−2 S/cm at 500 K (with an ion transport activation enthalpy of about 0.5–0.6 eV). Crystallized eutectics are superior to any single-phase M1−xRxF2+x solid solutions and ball-milling R1−yMyF3−y nanoceramics in terms of ion-conducting properties. These fluoride materials represent an alternative to widely applied tysonite-type ceramic composites in various electrochemical devices and require further in-depth studies. Full article
(This article belongs to the Section Composites Manufacturing and Processing)
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Graphical abstract

Graphical abstract
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<p>A schematic representation of the phase diagram of the BaF<sub>2</sub>–LaF<sub>3</sub> system [<a href="#B44-jcs-07-00330" class="html-bibr">44</a>]. Letters <span class="html-italic">F</span> and <span class="html-italic">T</span> denote the regions of SSs with fluorite- and tysonite-type structures, respectively; <span class="html-italic">E</span> is an eutectic point.</p>
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<p>The molar melt compositions and the appearance of the corresponding eutectic ingots synthesized by melt directional crystallization (<b>a</b>) and selected fabricated composite samples (<b>b</b>).</p>
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<p>The XRD patterns of eutectic composites. The positions of the Bragg peaks of the tysonite-type (<span class="html-italic">T</span>) and fluorite-type (<span class="html-italic">F</span>) phases for composite 70NdF<sub>3</sub> × 30SrF<sub>2</sub> are shown.</p>
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<p>Optical micrographs of longitudinal (<b>a</b>) and transverse (<b>b</b>–<b>d</b>) sections of the selected composite ingots. The length of the scale bar is 200 μm.</p>
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<p>SEM images of the typical morphology of longitudinal (<b>a</b>,<b>c</b>) and transverse (<b>b</b>,<b>d</b>) sections of the 68LaF<sub>3</sub> × 32BaF<sub>2</sub> and 59PrF<sub>3</sub> × 41CaF<sub>2</sub> eutectic ingots at different magnifications correspondingly. The length of the scale bar is 50 μm. The bright fields correspond to the <span class="html-italic">T</span>-phases.</p>
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<p>Temperature dependence of ionic conductivity of BaF<sub>2</sub>-based eutectic composites and selected compounds: <span class="html-italic">1</span>—68LaF<sub>3</sub> × 32BaF<sub>2</sub>, <span class="html-italic">2</span>—68CeF<sub>3</sub> × 32BaF<sub>2</sub>, <span class="html-italic">3</span>—69NdF<sub>3</sub> × 31BaF<sub>2</sub>, <span class="html-italic">4</span>—the fluorite-type Ba<sub>0</sub>.<sub>5</sub>La<sub>0</sub>.<sub>5</sub>F<sub>2</sub>.<sub>5</sub> single crystal [<a href="#B53-jcs-07-00330" class="html-bibr">53</a>], <span class="html-italic">5</span>—the tysonite-type La<sub>0</sub>.<sub>95</sub>Ba<sub>0</sub>.<sub>05</sub>F<sub>2</sub>.<sub>95</sub> single crystal [<a href="#B54-jcs-07-00330" class="html-bibr">54</a>], <span class="html-italic">6</span>—the ball-milling fluorite-type Ba<sub>0</sub>.<sub>5</sub>La<sub>0</sub>.<sub>5</sub>F<sub>2</sub>.<sub>5</sub> nanoceramics [<a href="#B55-jcs-07-00330" class="html-bibr">55</a>], and <span class="html-italic">7</span>—the ball-milling tysonite-type La<sub>0</sub>.<sub>9</sub>Ba<sub>0</sub>.<sub>1</sub>F<sub>2</sub>.<sub>9</sub> nanoceramics [<a href="#B55-jcs-07-00330" class="html-bibr">55</a>].</p>
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20 pages, 5984 KiB  
Article
Comparison of Granites from the Eastern and Western Districts of the Gejiu Ore District in South China: Implication for Petrogenesis and Tin Metallogeny
by Saijun Sun, Junjie Zhang, Shuang Li, Haobin Niu, Zhaojian Wu and Weidong Sun
Minerals 2023, 13(5), 691; https://doi.org/10.3390/min13050691 - 19 May 2023
Cited by 1 | Viewed by 1716
Abstract
Late Cretaceous granitoids are developed in the eastern and western districts of the Gejiu ore district, but tin deposits mainly occur in the eastern district, and the reasons for the difference in mineralization between the eastern and western districts are still controversial. Considering [...] Read more.
Late Cretaceous granitoids are developed in the eastern and western districts of the Gejiu ore district, but tin deposits mainly occur in the eastern district, and the reasons for the difference in mineralization between the eastern and western districts are still controversial. Considering the main factors controlling granite Sn fertility, the whole-rock geochemical characteristics of granites on both sides are compared. LA-ICP-MS zircon U-Pb analyses of the Gejiu granites yielded two age periods: the early phase from 79.2 to 83.3 Ma and the later phase from 73.8 to 75.6 Ma. The western district granites have higher zircon εHf(t), CaO/Na2O, Ba, and Sr concentrations and lower Rb/Sr ratios than the eastern district granites, indicating that the western district granites have more mantle-derived materials in the source than the eastern district granites. Results of oxygen fugacity show that the western granites have a higher oxygen fugacity condition. More depleted Ba, Sr, P, Eu and Ti characteristics with obviously negative Eu anomalies in the eastern granites also have high Rb/Sr ratios and low Nb/Ta and Zr/Hf ratios, indicating that the eastern granites experienced highly magmatic differentiation, attributed to high volatile F contents that can reduce the viscosity and solidus of magma. Combined with the differences in field observations and structural styles, on the whole, the western district granites have higher oxygen fugacities and lower F contents and magmatic differentiation than those in the eastern district granites, indicating that the western district granites are not conducive to mineralization. Full article
(This article belongs to the Special Issue Mineralization in Subduction Zone)
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Figure 1

Figure 1
<p>(<b>a</b>) Simplified map of main tectonic units in East Asia (modified after [<a href="#B16-minerals-13-00691" class="html-bibr">16</a>]). (<b>b</b>) Simplified geological map of Youjiang Basin displaying the distribution of late Cretaceous granitic rocks and related ore deposits (modified from [<a href="#B13-minerals-13-00691" class="html-bibr">13</a>,<a href="#B18-minerals-13-00691" class="html-bibr">18</a>]). (<b>c</b>) Simplified geological map of the Gejiu ore district (modified from [<a href="#B13-minerals-13-00691" class="html-bibr">13</a>,<a href="#B18-minerals-13-00691" class="html-bibr">18</a>]). ZDF, Ziyun–Du’an fault zone; PNF, Pingxiang–Nanling fault zone; HF, Honghe fault zone; MSF, Mile–Shizong fault zone.</p>
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<p>Hand specimen photographs and photomicrographs of porphyritic granites (<b>a</b>–<b>c</b>) and equigranular granites (<b>d</b>–<b>f</b>) from the Gejiu ore district. Bt, biotite; Kfs, K-feldspar; Mic, microcline; Ms, muscovite; Pl, plagioclase; Pth, perthite; Qtz, quartz; Ttn, titanite.</p>
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<p>(<b>a</b>) SiO<sub>2</sub> vs. K<sub>2</sub>O diagram of the granites from the Gejiu ore district. (<b>b</b>) A/NK vs. A/CNK diagram of granites from the Gejiu ore district. A/NK = Al<sub>2</sub>O<sub>3</sub>/(Na<sub>2</sub>O + K<sub>2</sub>O) (molar ratio), A/CNK = Al<sub>2</sub>O<sub>3</sub>/(CaO + Na<sub>2</sub>O + K<sub>2</sub>O) (molar ratio).</p>
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<p>Distributions of trace elements and REEs of granite from the Gejiu ore district [<a href="#B35-minerals-13-00691" class="html-bibr">35</a>]. (<b>a</b>) Spider diagram of trace elements; (<b>b</b>) Chondrite-normalized REE patterns.</p>
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<p>Concordia diagrams for zircons U-Pb ages (<sup>206</sup>Pb/<sup>238</sup>U-weighted average ages) from the (<b>a</b>) Longchahe, (<b>b</b>) Shenxianshui, (<b>c</b>) Baishachong, (<b>d</b>) Malage, (<b>e</b>) Songshujiao, (<b>f</b>) Kafang granite in the Gejiu ore district.</p>
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<p>(<b>a</b>) Classification of biotite in the Gejiu ore district (after [<a href="#B37-minerals-13-00691" class="html-bibr">37</a>,<a href="#B38-minerals-13-00691" class="html-bibr">38</a>]). (<b>b</b>) Diagram of Fe<sup>3+</sup>-Fe<sup>2+</sup>-Mg for biotite from granites in the Gejiu ore district [<a href="#B39-minerals-13-00691" class="html-bibr">39</a>]. (<b>c</b>) F vs. Cl diagram of biotite in the Gejiu ore district. Reference data come from [<a href="#B40-minerals-13-00691" class="html-bibr">40</a>].</p>
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<p>(<b>a</b>,<b>b</b>) ε<sub>Hf</sub>(<span class="html-italic">t</span>) vs. U–Pb age diagram of zircons in the Gejiu ore district. (<b>c</b>) T<sub>DM2</sub> vs. zircons U–Pb age in the Gejiu ore district. (<b>d</b>) Probability of Hf model age of zircons in the Gejiu ore district. Reference data come from [<a href="#B22-minerals-13-00691" class="html-bibr">22</a>].</p>
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<p>Whole-rock CaO/Na<sub>2</sub>O vs. Al<sub>2</sub>O<sub>3</sub>/TiO<sub>2</sub> (<b>a</b>), and Rb/Ba vs. Rb/Sr ratios (<b>b</b>). The diagrams are modified after [<a href="#B53-minerals-13-00691" class="html-bibr">53</a>].</p>
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<p>(<b>a</b>) Ce<sup>4+</sup>/Ce<sup>3+</sup> ratios vs. δEu, and (<b>b</b>) lgƒO<sub>2</sub> vs. temperatures of zircons from the Gejiu ore district. Reference data come from [<a href="#B22-minerals-13-00691" class="html-bibr">22</a>].</p>
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<p>Selected major and trace element Harker diagrams of the granites from the Gejiu ore district (whole-rock data). (<b>a</b>) P<sub>2</sub>O<sub>5</sub> vs. SiO<sub>2</sub>; (<b>b</b>) TiO<sub>2</sub> vs. SiO<sub>2</sub>; (<b>c</b>) Mg<sup>#</sup> vs. SiO<sub>2</sub>; (<b>d</b>) Sr vs. SiO<sub>2</sub>; (<b>e</b>) La<sub>N</sub>/Yb<sub>N</sub> vs. SiO<sub>2</sub>; (<b>f</b>) δEu vs. SiO<sub>2</sub>.</p>
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<p>(<b>a</b>) Diagram of Rb vs. Sr, and (<b>b</b>) Zr/Hf vs. Nb/Ta of granites from the Gejiu ore district (whole-rock data).</p>
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<p>Schematic map illustrating the northward subduction of the Neo-Tethys plate beneath the South China Block (modified from [<a href="#B23-minerals-13-00691" class="html-bibr">23</a>]). The red triangle cones are magmatism and Sn-W deposits.</p>
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12 pages, 4987 KiB  
Article
Printing Formation of Flexible (001)-Oriented PZT Films on Plastic Substrates
by Tomohiko Nakajima and Yuuki Kitanaka
Materials 2023, 16(5), 2116; https://doi.org/10.3390/ma16052116 - 6 Mar 2023
Cited by 1 | Viewed by 1620
Abstract
High-quality, uniaxially oriented, and flexible PbZr0.52Ti0.48O3 (PZT) films were fabricated on flexible RbLaNb2O7/BaTiO3 (RLNO/BTO)-coated polyimide (PI) substrates. All layers were fabricated by a photo-assisted chemical solution deposition (PCSD) process using KrF laser irradiation [...] Read more.
High-quality, uniaxially oriented, and flexible PbZr0.52Ti0.48O3 (PZT) films were fabricated on flexible RbLaNb2O7/BaTiO3 (RLNO/BTO)-coated polyimide (PI) substrates. All layers were fabricated by a photo-assisted chemical solution deposition (PCSD) process using KrF laser irradiation for photocrystallization of the printed precursors. The Dion–Jacobson perovskite RLNO thin films on flexible PI sheets were employed as seed layers for the uniaxially oriented growth of PZT films. To obtain the uniaxially oriented RLNO seed layer, a BTO nanoparticle-dispersion interlayer was fabricated to avoid PI substrate surface damage under excess photothermal heating, and the RLNO has been orientedly grown only at around 40 mJ·cm−2 at 300 °C. The prepared RLNO seed layer on the BTO/PI substrate showed very high (010)-oriented growth with a very high Lotgering factor (F(010) = 1.0). By using the flexible (010)-oriented RLNO film on BTO/PI, PZT film crystal growth was possible via KrF laser irradiation of a sol–gel-derived precursor film at 50 mJ·cm−2 at 300 °C. The obtained PZT film showed highly (001)-oriented growth on the flexible plastic substrates with F(001) = 0.92 without any micro-cracks. The RLNO was only uniaxial-oriented grown at the top part of the RLNO amorphous precursor layer. The oriented grown and amorphous phases of RLNO would have two important roles for this multilayered film formation: (1) triggering orientation growth of the PZT film at the top and (2) the stress relaxation of the underneath BTO layer to suppress the micro-crack formation. This is the first time that PZT films have been crystallized directly on flexible substrates. The combined processes of photocrystallization and chemical solution deposition are a cost-effective and highly on-demand process for the fabrication of flexible devices. Full article
(This article belongs to the Section Energy Materials)
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Figure 1

Figure 1
<p>Flow chart of fabrication procedure for the PZT/RLNO/BTO/PI layer structure.</p>
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<p>(<b>a</b>) XRD pattern irradiated laser fluence dependence for RLNO films on BTO/PI substrates prepared by the PCSD process. (<b>b</b>) Schematic layers and crystal structure of RLNO. The dotted line in the inset represents the simple perovskite unit cell. (<b>c</b>) XRD 2θ-β map of an RLNO film on BTO/PI prepared at a fluence of 40 mJ·cm<sup>−2</sup>. (<b>d</b>) β-scan for the 020 reflection. The blue line indicates the fitting for full width at half maximum (FWHM) evaluation.</p>
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<p>Numerically simulated temperature maps with depth (<span class="html-italic">d</span>) and time (<span class="html-italic">t</span>) for the amorphous precursor RLNO thin film on the PI substrate irradiated by a 40-mJ·cm<sup>−2</sup> KrF laser pulse (<b>a</b>) without and (<b>b</b>) with the BTO interlayer.</p>
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<p>Optical microscope images for RLNO/BTO/PI prepared by KrF laser irradiation at (<b>a</b>) 40 mJ·cm<sup>−2</sup> and (<b>b</b>) 55 mJ·cm<sup>−2</sup>.</p>
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<p>(<b>a</b>) Numerically simulated temperature maps across depth (<span class="html-italic">d</span>) and time (<span class="html-italic">t</span>) for the amorphous precursor RLNO thin film on a BTO/PI substrate irradiated at a KrF laser fluence of 35–55 mJ·cm<sup>−2</sup>. (<b>b</b>) Time dependence at the interface between RLNO and BTO (<span class="html-italic">d</span> = 120 nm) and depth dependence (<span class="html-italic">t</span> = 90 ns) of simulated temperature for the RLNO/BTO layers irradiated at a KrF laser fluence of 35–55 mJ·cm<sup>−2</sup>.</p>
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<p>XRD patterns and 2θ-β maps for PZT films prepared by the PCSD process at 50 mJ·cm<sup>−2</sup> on BTO/PI substrates (<b>a</b>) without and (<b>b</b>) with (010)-oriented RLNO seed layers. The inset shows the β-scan for the 001 spot of the PZT and the 020 spot of the RLNO films.</p>
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<p>Optical microscope images for the PZT films prepared by the PCSD process at 50 mJ·cm<sup>−2</sup> (<b>a</b>) without and (<b>b</b>) (010)-oriented RLNO seed layers.</p>
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<p>XTEM image of the PZT/RLNO/BTO/PI and high-resolution lattice image at the interface between PZT and the (010)-oriented RLNO film surface. o- and np- represent “oriented” and “nanoparticle-derived”, respectively.</p>
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<p>Schematic illustration of the PZT/RLNO/BTO/PI layer structure with the role of each layer. o-, a-, and np- represent “oriented”, “amorphous”, and “nanoparticle-derived”, respectively.</p>
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11 pages, 2919 KiB  
Article
Multi-Mode Lanthanide-Doped Ratiometric Luminescent Nanothermometer for Near-Infrared Imaging within Biological Windows
by Hao Li, Esmaeil Heydari, Yinyan Li, Hui Xu, Shiqing Xu, Liang Chen and Gongxun Bai
Nanomaterials 2023, 13(1), 219; https://doi.org/10.3390/nano13010219 - 3 Jan 2023
Cited by 9 | Viewed by 2773
Abstract
Owing to its high reliability and accuracy, the ratiometric luminescent thermometer can provide non-contact and fast temperature measurements. In particular, the nanomaterials doped with lanthanide ions can achieve multi-mode luminescence and temperature measurement by modifying the type of doped ions and excitation light [...] Read more.
Owing to its high reliability and accuracy, the ratiometric luminescent thermometer can provide non-contact and fast temperature measurements. In particular, the nanomaterials doped with lanthanide ions can achieve multi-mode luminescence and temperature measurement by modifying the type of doped ions and excitation light source. The better penetration of the near-infrared (NIR) photons can assist bio-imaging and replace thermal vision cameras for photothermal imaging. In this work, we prepared core–shell cubic phase nanomaterials doped with lanthanide ions, with Ba2LuF7 doped with Er3+/Yb3+/Nd3+ as the core and Ba2LaF7 as the coating shell. The nanoparticles were designed according to the passivation layer to reduce the surface energy loss and enhance the emission intensity. Green upconversion luminescence can be observed under both 980 nm and 808 nm excitation. A single and strong emission band can be obtained under 980 nm excitation, while abundant and weak emission bands appear under 808 nm excitation. Meanwhile, multi-mode ratiometric optical thermometers were achieved by selecting different emission peaks in the NIR window under 808 nm excitation for non-contact temperature measurement at different tissue depths. The results suggest that our core–shell NIR nanoparticles can be used to assist bio-imaging and record temperature for biomedicine. Full article
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<p>(<b>a</b>) Morphological characterization of nanocrystals at 50 nm scales was obtained by TEM. (<b>b</b>) Morphological characterization of nanocrystals at 10 nm scales was obtained by TEM. The selective area electron diffraction (SAED) pattern is presented in the illustration on the upper right. (<b>c</b>) The high-resolution TEM (HR-TEM) image of Ba<sub>2</sub>LuF<sub>7</sub>@Ba<sub>2</sub>LaF<sub>7</sub>. (<b>d</b>) The particle size distribution plot for Ba<sub>2</sub>LuF<sub>7</sub>@Ba<sub>2</sub>LaF<sub>7</sub>. (<b>e</b>) XRDs of tri-doped Ba<sub>2</sub>LaF<sub>7</sub> and Ba<sub>2</sub>LuF<sub>7</sub>@Ba<sub>2</sub>LaF<sub>7</sub> nanocrystals were compared with those of standard cards. (<b>f</b>) Rietveld XRD refinement for Ba<sub>2</sub>LuF<sub>7</sub>@Ba<sub>2</sub>LaF<sub>7</sub> nanocrystals.</p>
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<p>(<b>a</b>) The emission spectra of Yb<sup>3+</sup>/Nd<sup>3+</sup> and Yb<sup>3+</sup>/Er<sup>3+</sup>/Nd<sup>3+</sup> codoped Ba<sub>2</sub>LaF<sub>7</sub> and Ba<sub>2</sub>LuF<sub>7</sub> nanoparticles, and the excitation light source wavelength is 808 nm. (<b>b</b>) Schematic illustration of the luminescent nanoparticles excited by 808 nm laser. (<b>c</b>) General energy level diagram of Er<sup>3+</sup>, Yb<sup>3+</sup>, and Nd<sup>3+</sup> ions.</p>
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<p>(<b>a</b>) Photoluminescence spectra curve of the Ba<sub>2</sub>LuF<sub>7</sub>: Yb<sup>3+</sup>/Nd<sup>3+</sup>/Er<sup>3+</sup> nanoparticles covering 308–528 K temperature range. Integrated upconversion intensities at 974 nm and 1052 nm. (<b>b</b>) Temperature dependence of the fluorescence ratio values of thermally coupled energy levels. (<b>c</b>) Ln(FIR) is an inverse absolute function of absolute temperature. (<b>d</b>) The temperature function of the thermal coupling level of nanomaterials based on the fitting of Sa and Sr values.</p>
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<p>(<b>a</b>) Photoluminescence emission spectra curve of the Ba<sub>2</sub>LuF<sub>7</sub>: Nd<sup>3+</sup>/Yb<sup>3+</sup>/Er<sup>3+</sup> nanoparticles covering 308–528 K temperature range. Integrated upconversion intensities at 1321 nm and 1527 nm. (<b>b</b>) Temperature dependence of the fluorescence ratio values of thermally coupled energy levels. Dependence of FIR values of the (<b>b</b>) thermally coupled levels on temperature. (<b>c</b>) Ln(FIR) as an inverse absolute function of inverse absolute temperature. (<b>d</b>) The temperature function of the thermal coupling level of nanomaterials based on the fitting of <span class="html-italic">S<sub>a</sub></span> and <span class="html-italic">S<sub>r</sub></span> values. <span class="html-italic">S<sub>a</sub></span> and <span class="html-italic">S<sub>r</sub></span> values are based on the (<b>d</b>) thermally coupled levels as a function of temperature.</p>
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<p>(<b>a</b>) The selected NIR imaging interval. (<b>b</b>) NIR luminescence of nanoparticles. (<b>c</b>) Schematic of biological tissue imaging of nanoparticles.</p>
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20 pages, 4261 KiB  
Article
National-Scale Geochemical Baseline of 69 Elements in Laos Stream Sediments
by Wei Wang, Xueqiu Wang, Bimin Zhang, Qiang Wang, Dongsheng Liu, Zhixuan Han, Sounthone LAOLO, Phomsylalai SOUKSAN, Hanliang Liu, Jian Zhou, Xinbin Cheng and Lanshi Nie
Minerals 2022, 12(11), 1360; https://doi.org/10.3390/min12111360 - 26 Oct 2022
Cited by 2 | Viewed by 2687
Abstract
Geochemical baselines are crucial to explore mineral resources and monitor environmental changes. This study presents the first Laos geochemical baseline values of 69 elements. The National-scale Geochemical Mapping Project of Lao People’s Democratic Republic conducted comprehensive stream sediment sampling across Laos, yielding 2079 [...] Read more.
Geochemical baselines are crucial to explore mineral resources and monitor environmental changes. This study presents the first Laos geochemical baseline values of 69 elements. The National-scale Geochemical Mapping Project of Lao People’s Democratic Republic conducted comprehensive stream sediment sampling across Laos, yielding 2079 samples collected at 1 sample/100 km2, and 69 elements were analyzed. Based on the results of LGB value, R-mode factor analysis, and scatter plot analysis, this paper analyzes the relationship between the 69 elements and the geological background, mineralization, hypergene processes and human activities in the study area. The median values of element contents related to the average crustal values were: As, B, Br, Cs, Hf, Li, N, Pb, Sb, Zr, and SiO2, >1.3 times; Ba, Be, Cl, Co, Cr, Cu, F, Ga, Mn, Mo, Ni, S, Sc, Sr, Ti, Tl, V, Zn, Eu, Al2O3, Tot.Fe2O3, MgO, CaO, and Na2O, <0.7 times; and Ag, Au, Bi, Cd, Ge, Hg, I, In, Nb, P, Rb, Se, Sn, Ta, Th, U, W, Y, La, Ce, Pr, Nd, Sm, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, and K2O, 0.7–1.3 times. R-mode factor analysis based on principal component analysis and varimax rotation showed that they fall into 12 factors related to bedrock, (rare earth, ferrum-group, and major Al2O3 and K2O elements; mineralization–Au, Sb, and As) and farming activities–N, Br, S, and C). This study provides basic geochemical data for many fields, including basic geology, mineral exploration, environmental protection and agricultural production in Laos. Full article
(This article belongs to the Special Issue Critical Metal Minerals)
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<p>Tectonic sketch of Laos (modified from [<a href="#B27-minerals-12-01360" class="html-bibr">27</a>,<a href="#B28-minerals-12-01360" class="html-bibr">28</a>]). Tectonic units: 1—Jinghong-Sukhothai arc; 2—Simao-Phitsanulok block; 3—Vientiane-Kontum block; 4—Truong Son block; 5—DienBienPhu-Loei suture; 6—Sepon-TamKy suture; 7—Ailaoshan-Song Ma procedure. Faults: F1—Lancangjiang-Ban Namkham fault; F2—Nam Beng fault; F3—Louangphrabang fault; F4—Phu Pulei fault; F5—Truong Son-Da Nang fault; F6—Song Lan fault; F7—Song Ma fault.</p>
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<p>Grid cell (<b>a</b>) and sample location layout (<b>b</b>). Black arrows indicate the directions of the river.</p>
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<p>Sample sites of the National-scale Geochemical Mapping Project of Lao PDR (NGMPL).</p>
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<p>(<b>a</b>) Histogram and boxplot of Au on the raw data, (<b>b</b>) Histogram and boxplot of Sn on the raw data, (<b>c</b>) Histogram of Au on the clr-transformed data, (<b>d</b>) Histogram of Sn on the clr-transformed data. Asterisks indicate cases with values more than 1.5 times box length from the upper edge of the box.</p>
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<p>Bar graph showing the enrichment/depletion of the 69 elements using the ratio of the median and the CA (<b>upper</b>) and CGB (<b>top</b>) values.</p>
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<p>Biplot of Factor 1 (Bi−Th−U−W−Cs−K<sub>2</sub>O−Rb−Tl−(V−Cr−Cu−Ni −Co−Ti−TFe<sub>2</sub>O<sub>3</sub>)) vs. Factor 2 (Er−Tm−Ho−Yb−Lu−Y−Dy−Tb−Gd association). Circles indicate elements.</p>
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<p>Chondrite-normalized REEs diagrams. (Chondrite and PAAS data after [<a href="#B54-minerals-12-01360" class="html-bibr">54</a>,<a href="#B55-minerals-12-01360" class="html-bibr">55</a>]). REEs, LREEs, HREEs are expressed in mg/kg; N: chondrites; NGMPL: The National-Scale Geochemical Mapping Project in Lao PDR; CGB: China Geochemical Baselines value [<a href="#B19-minerals-12-01360" class="html-bibr">19</a>]; SSC: Stream sediment in South China [<a href="#B56-minerals-12-01360" class="html-bibr">56</a>]; PAAS: Australian Post-Archean average shale [<a href="#B55-minerals-12-01360" class="html-bibr">55</a>]; CA: Average crustal values [<a href="#B17-minerals-12-01360" class="html-bibr">17</a>].</p>
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<p>Biplot of Factor 2 vs. Factor 4 indicating the fractionation of LREEs and HREEs. Circles indicate elements.</p>
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<p>Biplot of Factor 3 (SiO<sub>2</sub>−Ge−Cl−Ag−Zr association) vs. Factor 12 (Au). Circles indicate elements.</p>
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<p>Biplot of Factor 1(Bi−Th−U−W−Cs−K<sub>2</sub>O−Rb−Tl−(V−Cr−Cu−Ni−Co−Ti−TFe<sub>2</sub>O<sub>3</sub>) association) vs. Factor 3 (SiO<sub>2</sub>−Ge−Cl−Ag−Zr association). Circles indicate elements.</p>
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<p>(<b>a</b>) Correlation scatter diagram between C and N, (<b>b</b>) Correlation scatter diagram between P and N, (<b>c</b>) Correlation scatter diagram between C and P, (<b>d</b>) Correlation scatter diagram between C and CaO.</p>
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<p>Correlation of C and Br contents in stream sediments from NGMPL.</p>
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<p>Biplot of F5 (TC−N−S−Br−I−Se association) vs. F10 (Al<sub>2</sub>O<sub>3</sub>). Circles indicate elements.</p>
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8 pages, 1162 KiB  
Article
Co-Doping Effect on the Optical Properties of Eu(2+/3+) Doped in BaSiO3
by Purevdulam Namkhai and Kiwan Jang
Materials 2022, 15(19), 6559; https://doi.org/10.3390/ma15196559 - 21 Sep 2022
Cited by 1 | Viewed by 1069
Abstract
To investigate the effect of co-doping on the optical properties of Eu(2+/3+) doped in Ba0.98SiO3:0.02Eu, the series of Ba0.96SiO3:0.02Eu, 0.02R+/3+ (R+ = Li+, K+ or [...] Read more.
To investigate the effect of co-doping on the optical properties of Eu(2+/3+) doped in Ba0.98SiO3:0.02Eu, the series of Ba0.96SiO3:0.02Eu, 0.02R+/3+ (R+ = Li+, K+ or Na+, R3+ = La3+ or Y3+) phosphors were synthesized using a solid-state reaction method. The excitation efficiency due to the charge transfer band (CTB) was enhanced via co-doping of R+ and the emission intensity due to Eu3+ was thus increased by 3.7 times compared with that of the single-doped Ba0.98SiO3:0.02Eu3+. However, the co-doping of R+ does not increase the emission intensity of Eu3+ via the direct 7F05L6 excitation of Eu3+, but rather decreases it. On the other hand, the emission intensities due to Eu2+ were decreased via the co-doping of R+ but increased via the co-doping of La3+. The present work reveals that the optical properties of Eu3+ or Eu2+ doped in BaSiO3 depend not on the charge state (+ or 3+) of the co-doped ions, but on the co-doped element itself. Full article
(This article belongs to the Special Issue High-Efficiency Light-Emitting Materials and Devices)
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<p>XRD patterns of Ba<sub>0</sub>.<sub>98</sub>SiO<sub>3</sub>:0.02Eu<sup>3+</sup>, 0.02R (R = Li<sup>+</sup>, K<sup>+</sup> and Na<sup>+</sup>).</p>
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<p>Excitation spectra (<b>a</b>) obtained by monitoring the emission at 612 nm, emission spectra at an excitation wavelength of (<b>b</b>) 230 nm and (<b>c</b>) 393 nm for Ba<sub>0</sub>.<sub>96</sub>SiO<sub>3</sub>:0.02Eu<sup>3+</sup>, 0.02R<sup>+/3+</sup> phosphors (samples 1–7).</p>
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<p>Effect of co-doping on the PL intensity of Eu<sup>3+</sup> ions excited by 230 nm and 393 nm, respectively.</p>
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<p>Excitation (<b>a</b>) and emission (<b>b</b>–<b>d</b>) spectra of the Ba<sub>0</sub>.<sub>96</sub>SiO<sub>3</sub>:0.02Eu<sup>2+</sup>, 0.02R<sup>+/3+</sup> phosphors (samples 8–14).</p>
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17 pages, 3834 KiB  
Article
Structural, Magnetic, and Electrical Properties and Magnetoresistance of Monovalent K-Substituted La0.7Ba0.3−xKxMnO3 (x = 0 and 0.04) Manganite
by Amirah Zahrin, Nurul Atiqah Azhar, Norazila Ibrahim and Zakiah Mohamed
Condens. Matter 2022, 7(3), 51; https://doi.org/10.3390/condmat7030051 - 24 Aug 2022
Cited by 8 | Viewed by 2401
Abstract
The effects of K+ substitution at the Ba-site on the structural, magnetic, and electrical properties and magnetoresistance (MR) of La0.7Ba0.3xKxMnO3 (x = 0 and 0.04) manganites prepared via the solid-state method were [...] Read more.
The effects of K+ substitution at the Ba-site on the structural, magnetic, and electrical properties and magnetoresistance (MR) of La0.7Ba0.3xKxMnO3 (x = 0 and 0.04) manganites prepared via the solid-state method were investigated. Rietveld refinement of X-ray diffraction data confirmed that both samples were crystallized in the rhombohedral structure with the R3c¯ space group. In addition, the unit cell volume, V, and the average grain size also increased with K+ ions. Magnetization versus applied field (MH) measurement was carried out, and the saturation magnetization (Ms) was found to increase from 1.81 μB/f.u. (x = 0) to 4.11 μB /f.u. (x = 0.04), implying that K+ ions strengthened the ferromagnetic (FM) interaction. Furthermore, the metal–insulator transition temperature, TMI, increased from 257 K (x = 0) to 271 K (x = 0.04). The observed behaviour may be related to the enhancement of double-exchange (DE) interaction due to the increase in Mn-O-Mn bond angle and electronic bandwidth (W), favouring the increasing rate of the eg electron hopping process. The fitting of the electrical resistivity data in the metallic region describes the significance of residual resistivity, electron–electron and electron–magnon scattering processes to elucidate the electronic transport properties. Within the insulating region, variable range hopping (VRH) and small polaron hopping (SPH) models are proposed to describe the conduction mechanism. Full article
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<p>Rietveld refinement of the XRD patterns for La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04). The solid red line represents the observed data, the black line corresponds to the calculated data, whilst the blue lines correspond to the difference between the observed and calculated data. Tick marks (vertical) indicate the allowed Bragg position. The presence of minor additional Mn<sub>3</sub>O<sub>4</sub> peak was indicated by the “*” symbol.</p>
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<p>Variation of K concentration, <span class="html-italic">x</span>, with (<b>a</b>) lattice parameter a, b, c, and (<b>b</b>) volume in La<sub>0.7</sub>Ba<sub>0.3−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04) sample.</p>
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<p>SEM-EDX analysis of La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> for (<b>a</b>) <span class="html-italic">x</span>= 0 and (<b>b</b>) <span class="html-italic">x</span> = 0.04 samples.</p>
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<p>Temperature dependence of real part of AC susceptibility (χ′) graph for La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04).</p>
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<p>Magnetization, M, versus applied magnetic field, H, up to ±14 kOe for La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04). The inset shows the enlarged view of the M–H loop for the lower magnetic field.</p>
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<p>Temperature dependence of resistivity graph for La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04) under the absence of magnetic field.</p>
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<p>Temperature dependence of resistivity graph for (<b>a</b>) <span class="html-italic">x</span> = 0 and (<b>b</b>) <span class="html-italic">x</span> = 0.04 in magnetic fields of 0 T and 0.8 T. The solid linear fit (black lines) corresponded to the fitting with Equation (4).</p>
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<p>The resistivity data fitting according to SPH model for (<b>a</b>) <span class="html-italic">x</span> = 0 and (<b>b</b>) <span class="html-italic">x</span> = 0.04.</p>
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<p>The resistivity data fitting according to VRH model for (<b>a</b>) <span class="html-italic">x</span> = 0 and (<b>b</b>) <span class="html-italic">x</span> = 0.04.</p>
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<p>Temperature dependence of MR (%) for La<sub>0.7</sub>Ba<sub>0.3</sub><sub>−<span class="html-italic">x</span></sub>K<span class="html-italic"><sub>x</sub></span>MnO<sub>3</sub> (<span class="html-italic">x</span> = 0 and 0.04) under H = 0.8 T.</p>
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28 pages, 5511 KiB  
Article
Mineral Chemistry of Pyrochlore Supergroup Minerals from the Boziguoer Nb-Ta-Zr-Rb-REE Deposit, NW China: Implications for Nb Enrichment by Alkaline Magma Differentiation
by Zhenghao Sun, Kezhang Qin, Yajing Mao, Dongmei Tang, Fangyue Wang, Noreen J. Evans and Qifeng Zhou
Minerals 2022, 12(7), 785; https://doi.org/10.3390/min12070785 - 21 Jun 2022
Cited by 6 | Viewed by 2398
Abstract
Alkaline rocks are generally enriched in rare metals (e.g., Nb, Ta, and Zr) and rare earth elements (REE), but the key factors controlling Nb-Ta-REE enrichment remain unclear. The Boziguoer Nb (Ta-Zr-Rb-REE) deposit in Southwest Tianshan (northern margin of Tarim Basin) is China’s largest, [...] Read more.
Alkaline rocks are generally enriched in rare metals (e.g., Nb, Ta, and Zr) and rare earth elements (REE), but the key factors controlling Nb-Ta-REE enrichment remain unclear. The Boziguoer Nb (Ta-Zr-Rb-REE) deposit in Southwest Tianshan (northern margin of Tarim Basin) is China’s largest, with reserves of 0.32 Mt Nb2O5 and 0.02 Mt Ta2O5. It is an alkaline felsic complex 4.45 km in length and 0.5–1.3 km in width, composed of alkalic granite and syenite, which can be subdivided into syenite I and syenite II. The main minerals in each lithofacies are the same (albite, K-feldspar, quartz, arfvedsonite and aegirine). The Nb in the deposit is mainly hosted in pyrochlore supergroup minerals, ubiquitous in alkalic granite and syenite of the Boziguoer deposit. The wide variation in cations (Ca, Na, REE, U, Th) in the A-site further classifies the Boziguoer pyrochlore supergroup minerals as fluornatropyrochlore, fluorcalciopyrochlore and fluorkenopyrochlore. All Boziguoer pyrochlore supergroup minerals are Nb-rich and Ta-poor at the B-site and dominated by F at the Y-site. These cation occurrence illustrate a new mechanism of substitution in the Boziguoer pyrochlore supergroup minerals (2Ca2+ +Ti4+ +4Ta5+ = REE3+ +A-V + 5Nb5+, where A-V is the A-site vacancy). This substitution mechanism is different from that in the pyrochlore supergroup minerals from other rocks such as carbonatite and nepheline syenite, which are dominated by the replacement of Ba (Rb, Sr) with Ca+ Na + A-V. In addition, the substitution of REE (mainly La, Ce) for Ca in the Boziguoer pyrochlore supergroup minerals is likely a result of either REE enrichment or a change in the REE partition coefficient during the evolution of the alkaline magma. Both the pyrochlore supergroup minerals and their host rocks display negative large ion lithophile element (LILE; K, Rb, Sr, and Ba) anomalies, positive high-field-strength element (HFSE) anomalies and light rare earth element (LREE) enrichment with negative Eu anomalies. This is consistent with the crystallization of the pyrochlore supergroup minerals from the magma rather than from hydrothermal fluids, suggesting a magmatic origin. These findings indicate that the mechanisms of pyrochlore supergroup minerals crystallization in alkaline magma may be significantly different from those in carbonatite and nepheline syenite, and that magmatic differentiation processes may have played a role in the enrichment of the Boziguoer deposit by Nb. Full article
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<p>(<b>a</b>) Tectonic units and location of Southern Tianshan region in Xinjiang, NW China (modified from [<a href="#B58-minerals-12-00785" class="html-bibr">58</a>]); (<b>b</b>) distribution of the Boziguoer deposit in the Southern Tianshan region and coeval alkaline felsic rocks in the Tarim north rim (modified from [<a href="#B60-minerals-12-00785" class="html-bibr">60</a>,<a href="#B61-minerals-12-00785" class="html-bibr">61</a>]).</p>
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<p>Simplified geologic map of the Boziguoer intrusion and sample locations (modified after [<a href="#B28-minerals-12-00785" class="html-bibr">28</a>,<a href="#B29-minerals-12-00785" class="html-bibr">29</a>]).</p>
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<p>Hand sample images and microphotographs of main rocks of the Boziguoer intrusion. (<b>a</b>,<b>b</b>) = Alkalic granite facies; (<b>c</b>,<b>d</b>) = syenite facies I; (<b>e</b>,<b>f</b>) = syenite facies II. Abbreviations: Q = quartz, Ab = albite, Kf = K-feldspar, Aeg = aegirine, Arf = arfvedsonite.</p>
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<p>Microphotographs showing the textures of Boziguoer alkaline granite ((<b>a</b>,<b>d</b>) = alkalic granite facies, (<b>b</b>,<b>e</b>) = syenite facies I, (<b>c</b>,<b>f</b>) = syenite facies II). Arf = arfvedsonite, Aeg = aegirine, Ast = astrophyllite, Qz = quartz, Or = orthoclase, Ab = albite, Pcl = pyrochlore supergroup minerals.</p>
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<p>Variation in selected elements (apfu) in pyrochlore supergroup minerals from Boziguoer deposit. (<b>a</b>) Ti is negatively correlated with Nb, R<sup>2</sup> is 0.88; (<b>b</b>) Ta is negatively correlated with Nb, R<sup>2</sup> is 0.50; (<b>c</b>) Ca is negatively correlated with Nb, R<sup>2</sup> is 0.81; (<b>d</b>) F is positively correlated with Nb, R<sup>2</sup> is 0.71; (<b>e</b>) La+Ce is positively correlated with Nb, R<sup>2</sup> is 0.56; (<b>f</b>) A-vacancies is positively correlated with Nb, R<sup>2</sup> is 0.61.</p>
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<p>Variation in selected elements (apfu) in pyrochlore supergroup minerals from Boziguoer deposit.</p>
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<p>Triangular Nb–Ti–Ta pyrochlore classification scheme (modified by [<a href="#B30-minerals-12-00785" class="html-bibr">30</a>,<a href="#B40-minerals-12-00785" class="html-bibr">40</a>,<a href="#B66-minerals-12-00785" class="html-bibr">66</a>,<a href="#B69-minerals-12-00785" class="html-bibr">69</a>,<a href="#B70-minerals-12-00785" class="html-bibr">70</a>]).</p>
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<p>Ternary plot of Ca, Na and A-site vacancy (modified from [<a href="#B36-minerals-12-00785" class="html-bibr">36</a>]). The magmatic, hydrothermal and supergene fields of pyrochlore supergroup minerals (black circles) are from [<a href="#B36-minerals-12-00785" class="html-bibr">36</a>]. The black arrow indicates the compositional evolution of pyrochlore supergroup minerals from carbonatite. The magmatic field of pyrochlore supergroup minerals from the Boziguoer deposit (red circle) is proposed based on the results presented in this study. The red arrow indicates their compositional evolution. The pyrochlore supergroup mineral data for carbonatite are from [<a href="#B23-minerals-12-00785" class="html-bibr">23</a>,<a href="#B31-minerals-12-00785" class="html-bibr">31</a>,<a href="#B37-minerals-12-00785" class="html-bibr">37</a>,<a href="#B41-minerals-12-00785" class="html-bibr">41</a>]; data for nepheline syenite are from [<a href="#B35-minerals-12-00785" class="html-bibr">35</a>].</p>
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<p>Chondrite-normalized REE patterns and primitive mantle-normalized trace element patterns for Boziguoer pyrochlore supergroup minerals and the host rock. The chondrite and primitive mantle values are from [<a href="#B71-minerals-12-00785" class="html-bibr">71</a>].</p>
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<p>Tetrad τ coefficients for pyrochlore supergroup minerals and their host rocks. The first to fourth tetrad coefficients are shown, respectively.</p>
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12 pages, 3668 KiB  
Article
MSR Simulation with cGEMS: Fission Product Release and Aerosol Formation
by Sergii Nichenko, Jarmo Kalilainen and Terttaliisa Lind
J. Nucl. Eng. 2022, 3(1), 105-116; https://doi.org/10.3390/jne3010006 - 17 Mar 2022
Viewed by 2258
Abstract
The release of fission products and fuel materials from a molten-salt fast-reactor fuel in hypothetical accident conditions was investigated. The molten-salt fast reactor in this investigation features a fast neutron spectrum, operating in the thorium cycle, and it uses LiF-ThF4-UF4 [...] Read more.
The release of fission products and fuel materials from a molten-salt fast-reactor fuel in hypothetical accident conditions was investigated. The molten-salt fast reactor in this investigation features a fast neutron spectrum, operating in the thorium cycle, and it uses LiF-ThF4-UF4 as a fuel salt. A coupling between the severe accident code MELCOR and thermodynamical equilibrium solver GEMS, the so-called cGEMS, with the updated HERACLES database was used in the modeling work. The work was carried out in the frame of the EU SAMOSAFER project. At the beginning of the simulation, the fuel salt is assumed to be drained from the reactor to the bottom of a confinement building. The containment atmosphere is nitrogen. The fission products and salt materials are heated by the decay heat, and due to heating, they are evaporated from the surface of a molten salt pool. The chemical system in this investigation included the following elements: Li, F, Th, U, Zr, Np, Pu, Sr, Ba, La, Ce, and Nd. In addition to the release of radioactive materials from the fuel salt, the formation of aerosols and the vapor-phase species in the modeled confinement were determined. Full article
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Figure 1

Figure 1
<p>General schematics of the cGEMS [<a href="#B11-jne-03-00006" class="html-bibr">11</a>].</p>
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<p>Schematic of the MELCOR model of the confinement [<a href="#B12-jne-03-00006" class="html-bibr">12</a>].</p>
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<p>Total amount of salt material and actinides released from the salt in the base-case simulation (left <span class="html-italic">y</span>-axis). Salt temperature, T, is given on the right <span class="html-italic">y</span>-axis.</p>
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<p>Total amount of salt material and actinides released from the salt in the over-fluorinated (F + 1%) simulation.</p>
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<p>Total amount of salt material and actinides released from the salt in the under-fluorinated (F 2− 1%) simulation.</p>
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<p>Total amount of fission products released from the salt in the base-case simulation.</p>
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<p>Total mass of aerosol air-borne in the confinement in the base-case simulation.</p>
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<p>Total mass of aerosol air-borne in the confinement in the over-fluorinated (+1%) simulation.</p>
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<p>Average mass median diameter (MMD) of aerosol in the confinement.</p>
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