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17 pages, 8610 KiB  
Article
Mechanisms Underlying Phase Transition and Regulation of Tantalum Powder Properties During Magnesium Thermal Reduction of Ta2O5 in a Molten Salt Medium
by Yi Chen, Zhenghao Han, Tianchen Li, Ruifang Wang, Chao Zhang, Yusi Che and Jilin He
Materials 2025, 18(5), 1115; https://doi.org/10.3390/ma18051115 - 1 Mar 2025
Viewed by 145
Abstract
Magnesium reduction of Ta2O5 (tantalum pentoxide) is a metallurgical process widely used to extract metallic tantalum powder from its oxide form using magnesium as a reducing agent in a molten salt medium. This study explores the mechanisms and patterns of [...] Read more.
Magnesium reduction of Ta2O5 (tantalum pentoxide) is a metallurgical process widely used to extract metallic tantalum powder from its oxide form using magnesium as a reducing agent in a molten salt medium. This study explores the mechanisms and patterns of phase transformation during the magnesium reduction of Ta2O5 in a molten salt medium, focusing on the influence of temperature and time on the physical and chemical properties of the resulting tantalum powder. The results reveal that under various reaction conditions in a molten salt medium, the magnesium reduction of Ta2O5 follows four distinct pathways: Ta2O5 → Ta, Ta2O5 → MgTa2O6 → Ta, Ta2O5 → MgTa2O6 → Mg4Ta2O9 → Ta, and Ta2O5 → Mg4Ta2O9 → Ta. Each pathway significantly affects the physical and chemical properties of the resulting tantalum powder. Using a uniform mixing method, the reaction proceeds directly from Ta2O5 to Ta powder in a single step. As the reaction temperature increases from 600 °C to 900 °C, the average particle size of the tantalum powder enlarges from 30 nm to 150 nm, with the product phase transitioning from a mixture of Ta and Ta2O to a single Ta phase. Additionally, prolonged holding time improves the uniformity of the tantalum powder’s particle distribution. This study accomplishes directional control over the phase transformation and the properties of tantalum powder during the reduction process, thus offering valuable guidance for the preparation of high-performance tantalum powder. Full article
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Graphical abstract

Graphical abstract
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<p>SEM-EDS results (<b>a</b>) and XRD patterns (<b>b</b>) of experimental tantalum pentoxide.</p>
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<p>Spreading of raw materials in the crucible; (<b>a</b>) Tantalum pentoxide on the bottom; (<b>b</b>) Tantalum pentoxide on the top; (<b>c</b>) homogeneous mixture.</p>
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<p>Standard Gibbs free energy change (<b>a</b>) and standard molar enthalpy change (<b>b</b>) for the magnesium reduction of tantalum oxide as a function of temperature.</p>
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<p>Effect of content of magnesium and potassium chloride on the adiabatic temperature of the system: (<b>a</b>) 3D surface view; (<b>b</b>) top view; (<b>c</b>) main view; and (<b>d</b>) side view.</p>
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<p>XRD patterns of the products before and after acid washing (placement method A). (<b>a</b>) after reduction; (<b>b</b>) after acid washing.</p>
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<p>SEM images showing morphology of pickling products (of placement method A) at different holding time conditions: (<b>a</b>) 0 h; (<b>b</b>) 1 h; (<b>c</b>) 3 h; and (<b>d</b>) 5 h.</p>
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<p>XRD patterns of the products before and after acid washing (placement method B). (<b>a</b>) after reduction; (<b>b</b>) after acid washing.</p>
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<p>SEM images showing morphology of pickling products (of placement method B) at different holding time conditions: (<b>a</b>) 0 h; (<b>b</b>) 1 h; (<b>c</b>) 3 h; and (<b>d</b>) 5 h.</p>
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<p>XRD patterns of the products obtained after acid washing (in placement method C).</p>
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<p>Comparison of particle size distribution (measured using Laser particle size analyzer) of pure metallic tantalum powder synthesized at 900 °C under different holding times, in placement methods B and C.</p>
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<p>Principle of phase transition during magnesium reduction of tantalum pentoxide. Different routes highlight the diffusion of magnesium for complete reduction of Ta<sub>2</sub>O<sub>5</sub> to Ta.</p>
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<p>XRD patterns of the products: (<b>a</b>) before and (<b>b</b>) after pickling at different reduction temperatures.</p>
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<p>Change in oxygen content at different reaction temperatures (<b>a</b>); Plot of ln k vs. 1/T×10<sup>3</sup> for the estimation of the activation energy of the reduced Ta powder (<b>b</b>).</p>
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<p>SEM images showing the morphology of the products: (<b>a</b>,<b>c</b>,<b>e</b>,<b>g</b>) before and (<b>b</b>,<b>d</b>,<b>f</b>,<b>h</b>) after pickling at different reduction temperatures.</p>
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<p>SEM images showing morphology of the products: (<b>a</b>,<b>c</b>) before and (<b>b</b>,<b>d</b>) after pickling at 900 °C for different holding times of (<b>a</b>,<b>b</b>) 1 h and (<b>c</b>,<b>d</b>) 5 h.</p>
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25 pages, 2866 KiB  
Article
Investigation of Select Pure Earth Metals as Redox Catalytic Electrodes in Single Compartment Hydrogen Peroxide Fuel Cells
by Faraz Alderson, Raveen Appuhamy and Stephen Andrew Gadsden
Appl. Sci. 2025, 15(4), 1857; https://doi.org/10.3390/app15041857 - 11 Feb 2025
Viewed by 507
Abstract
Hydrogen peroxide is a promising alternative to hydrogen gas for fuel cells, as it can act as the oxidizing and reducing agent and be stored in a stable liquid form, it simplifies the structure of the fuel cell. This study aims to investigate [...] Read more.
Hydrogen peroxide is a promising alternative to hydrogen gas for fuel cells, as it can act as the oxidizing and reducing agent and be stored in a stable liquid form, it simplifies the structure of the fuel cell. This study aims to investigate the use of antimony, bismuth, indium, tantalum, silver, dysprosium, erbium, gadolinium, holmium, and terbium as electrodes for the first time in a single-compartment hydrogen peroxide fuel cell. In this study, the procedure for custom electrodes for these metals is documented. The performance of the electrodes was evaluated by measuring the open circuit potential, comparing the cyclic voltammograms and observing the physical reactions of the cell combinations. The results of the study show the catalytic reaction is likely due to the formation of molecular oxide layers on the electrode surface. It was evident that an acidic peroxide electrolyte favors the best catalytic reaction. Tantalum and antimony were found to be the best-performing electrodes in this electrolyte, providing the best stability and performance. Full article
(This article belongs to the Section Energy Science and Technology)
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Figure 1

Figure 1
<p>Steps of fabricating metal electrodes. (<b>a</b>) An electrode metal joined to the copper rod using silver paste; (<b>b</b>) the casting of each electrode into jackets filled with epoxy resin; (<b>c</b>) a fully fabricated electrode before sanding and polishing; (<b>d</b>) a fully fabricated electrode after sanding, final polishing, and cleansing.</p>
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<p>Photographs of unpolished electrode tips after assembly next to a metric size scale.</p>
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<p>A three-electrode cell setup attached to potentiostat for voltammetry tests. The blue cable is for the working electrode, the red cable is for the counter electrode, and the black cable connects to the reference electrode.</p>
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<p>Corrosion on polished nickel ribbon three minutes after submersion in the Acidic Electrolyte 2. The corroded surface is visible with a light brown discolouration. Corrosion interferes with the chemical reaction so should be mitigated as much as possible.</p>
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<p>Open circuit potentials of electrodes in Alkaline Electrolyte. This depicts which electrodes have the largest potential when attached to a common reference electrode. Tb and Ta have the highest open circuit potential.</p>
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<p>Cyclic voltammograms of electrodes in Alkaline Electrolyte. Graphs (<b>a</b>–<b>c</b>) show overlaps of electrode voltammograms in Alkaline Electrolytes containing hydrogen peroxide. Graphs (<b>d</b>–<b>j</b>) show voltammograms for each electrode in Alkaline Electrolyte with and without hydrogen peroxide. Ta and Ho had the largest current densities during the potential sweep, demonstrating their favorable reactivity in alkaline electrolytes.</p>
Full article ">Figure 6 Cont.
<p>Cyclic voltammograms of electrodes in Alkaline Electrolyte. Graphs (<b>a</b>–<b>c</b>) show overlaps of electrode voltammograms in Alkaline Electrolytes containing hydrogen peroxide. Graphs (<b>d</b>–<b>j</b>) show voltammograms for each electrode in Alkaline Electrolyte with and without hydrogen peroxide. Ta and Ho had the largest current densities during the potential sweep, demonstrating their favorable reactivity in alkaline electrolytes.</p>
Full article ">Figure 6 Cont.
<p>Cyclic voltammograms of electrodes in Alkaline Electrolyte. Graphs (<b>a</b>–<b>c</b>) show overlaps of electrode voltammograms in Alkaline Electrolytes containing hydrogen peroxide. Graphs (<b>d</b>–<b>j</b>) show voltammograms for each electrode in Alkaline Electrolyte with and without hydrogen peroxide. Ta and Ho had the largest current densities during the potential sweep, demonstrating their favorable reactivity in alkaline electrolytes.</p>
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<p>Open circuit potentials of electrodes in Neutral Electrolyte vs. Acidic Electrolyte 1, where antimony had the highest cell output in the Acidic Electrolyte and tantalum had a higher cell output in the Neutral Electrolyte.</p>
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<p>Cyclic voltammograms of electrodes in the Neutral Electrolyte. Graph (<b>a</b>) shows the overlap of both Sb and Ta electrode voltammograms in the Neutral Electrolyte containing hydrogen peroxide. Graphs (<b>b</b>,<b>c</b>) show voltammograms for Sb and Ta electrodes in the Neutral Electrolyte with and without hydrogen peroxide. Testing the electrodes without hydrogen peroxide present in the electrolyte demonstrates the additional reactivity the compound adds to the reaction.</p>
Full article ">Figure 8 Cont.
<p>Cyclic voltammograms of electrodes in the Neutral Electrolyte. Graph (<b>a</b>) shows the overlap of both Sb and Ta electrode voltammograms in the Neutral Electrolyte containing hydrogen peroxide. Graphs (<b>b</b>,<b>c</b>) show voltammograms for Sb and Ta electrodes in the Neutral Electrolyte with and without hydrogen peroxide. Testing the electrodes without hydrogen peroxide present in the electrolyte demonstrates the additional reactivity the compound adds to the reaction.</p>
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<p>Cyclic voltammograms of electrodes in Acidic Electrolyte 1. Graph (<b>a</b>) shows overlap of both Sb and Ta electrode voltammograms in Acidic Electrode 1 containing hydrogen peroxide. Graphs (<b>b</b>,<b>c</b>) show voltammograms for Sb and Ta electrodes in Acidic Electrolyte 1 with and without hydrogen peroxide.</p>
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<p>Overlapping voltammograms of Ta electrode in peroxide electrolytes with three different pH values of 13.3 (alkaline), 7.0 (neutral), and 1.99 (acidic), showing that Tantalum had the highest current density in the alkaline electrolyte.</p>
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<p>Overlapping voltammograms of Sb electrode in peroxide electrolytes with two different pH values of 17.0 (neutral) and 1.99 (acidic), showing Sb is much more reactive in an acidic electrolyte.</p>
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<p>Proposed mechanism of hydrogen peroxide redox catalysis over electrode metal oxide surfaces in acidic pH. Metals include those tested in this chapter: Dy, Tb, Er, Ho, Gd, Ta, and Sb. MeXOA and MeYOB represent different oxides of the same metal at different oxidation states. Note that the novel electrode metals introduced in this chapter favor one of oxidation or reduction over the other, and not both simultaneously to then result in disproportionation.</p>
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10 pages, 2691 KiB  
Article
Size Dependence of the Band Gap of Core–Shell Tantalum and Tantalum Oxide (V) Nanoclusters
by Valentin A. Shilov, Petr V. Borisyuk, Diana V. Bortko, Smagul Karazhanov, Yuri Y. Lebedinskii and Oleg S. Vasilyev
Nanomaterials 2025, 15(1), 14; https://doi.org/10.3390/nano15010014 - 26 Dec 2024
Viewed by 456
Abstract
Monodisperse films of spherical tantalum oxide (V) nanoclusters and spherical tantalum nanoclusters with a tantalum oxide shell with diameters of 1.4–8 nm were obtained by magnetron sputtering. The size of the deposited nanoclusters was controlled using a quadrupole mass filter. The chemical composition [...] Read more.
Monodisperse films of spherical tantalum oxide (V) nanoclusters and spherical tantalum nanoclusters with a tantalum oxide shell with diameters of 1.4–8 nm were obtained by magnetron sputtering. The size of the deposited nanoclusters was controlled using a quadrupole mass filter. The chemical composition was certified using the XPS method. Using the Reflected Electron Energy Loss Spectroscopy (REELS), the dependence of the band gap width on the nanocluster size was determined. It was found that starting from a certain nanocluster size, the band gap width increases as the nanocluster size decreases. Based on experimental data and a theoretical model, the effective mass of electrons dependence as a function of nanocluster size was obtained. Full article
(This article belongs to the Special Issue Morphological Design and Synthesis of Nanoparticles (Second Edition))
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Figure 1

Figure 1
<p>Experimental setup diagram.</p>
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<p>Survey XPS spectrum of core–shell tantalum nanoclusters with diameter d = 3 nm.</p>
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<p>XPS spectrum of Ta+TaO<sub>x</sub> nanoclusters, Ta4f doublet.</p>
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<p>XPS spectrum of Ta<sub>2</sub>O<sub>5</sub> nanoclusters, Ta4f doublet.</p>
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<p>The dependence of TaO<sub>x</sub> shell thickness of Ta+TaO<sub>x</sub> core–shell nanocluster on nanocluster diameter.</p>
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<p>The blue line represents the REELS spectrum of a core–shell nanocluster sample with a nanocluster diameter of d = 4.5 nm. The red line represents the approximation of REELS data according to the model. The green vertical line represents the point of maximum elastic peak. The grey vertical line represents the model approximation region border. The blue vertical line represents the band gap region start.</p>
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<p>Dependence of the band gap width on the diameter of nanoclusters. Square markers indicate the band gap width for Ta+TaOx clusters, round markers indicate the band gap width for Ta<sub>2</sub>O<sub>5</sub> clusters, and the dotted line indicates the band gap width of bulk Ta<sub>2</sub>O<sub>5</sub>.</p>
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<p>Dependences of the effective mass of electrons in core–shell tantalum nanoclusters and Ta<sub>2</sub>O<sub>5</sub> nanoclusters on the cluster diameter.</p>
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37 pages, 28889 KiB  
Article
Pyrochlore-Supergroup Minerals and Their Relation to Columbite-Group Minerals in Peralkaline to Subaluminous A-Type Rare-Metal Granites with Special Emphasis on the Madeira Pluton, Amazonas, Brazil
by Karel Breiter, Hilton Tulio Costi and Zuzana Korbelová
Minerals 2024, 14(12), 1302; https://doi.org/10.3390/min14121302 - 23 Dec 2024
Viewed by 529
Abstract
Niobium (Nb) and tantalum (Ta) are quoted as “strategic” or “critical” elements for contemporaneous society. The main sources of Nb and Ta are minerals of the pyrochlore supergroup (PSGM) and the columbite group (CGM) mined from different magmatic lithologies. Textures and chemical compositions [...] Read more.
Niobium (Nb) and tantalum (Ta) are quoted as “strategic” or “critical” elements for contemporaneous society. The main sources of Nb and Ta are minerals of the pyrochlore supergroup (PSGM) and the columbite group (CGM) mined from different magmatic lithologies. Textures and chemical compositions of PSGM and CGM often provide key information about the origin of NbTa mineralization. Therefore, we decided to carry out a detailed study of the relations between the PSGM and CGM and their post-magmatic transformations, and the Madeira peralkaline pluton (Brazil) is an ideal object for such a study. Textures of the PSGM and CGM were studied using BSE imaging and SEM mapping, and their chemical compositions were determined using 325 electron microprobe analyses. Pyrochlore from the Madeira granite can be chemically characterized as Na, Ca-poor, U- and Pb-dominant, and Sn- and Zn-enriched; REE are enriched only during alteration. Two stages of alteration are present: (i) introduction of Fe + Mn, with the majority of them consumed by columbitization; (ii) introduction of Si and Fe, and in lesser amounts also Pb and U: Si, Pb, and U incorporated into pyrochlore, iron forming Fe-oxide halos around pyrochlore. During both stages, F and Na decreased. In the case of a (nearly) complete pyrochlore columbitization, U and Th were exsolved to form inclusions of a thorite/coffinite-like phase. In contrast to altered pyrochlores from other localities, pyrochlore from Madeira shows a relatively high occupancy of the A-site. Although Madeira melt was Na-, F-rich, contemporaneous crystallization of cryolite consumed both elements and pyrochlore was, from the beginning, relatively Na-, F-poor. Full article
(This article belongs to the Special Issue Rare-Metal Granites)
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Graphical abstract

Graphical abstract
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<p>Textures of the studied types of Madeira granites by automated mineralogy (TIMA): (<b>a</b>) hypersolvus granite; (<b>b</b>) core albite granite; (<b>c</b>) border albite granite. Explanation: dark blue—quartz, red—K-feldspar, light blue—albite, orange—fluorite, yellow—Li-mica, green—cryolite.</p>
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<p>Whole-rock geochemical characteristic of the studied rare-metal granites: (<b>a</b>) aluminum saturation index (ASI = Al/(Na + K + 0.5Ca) mol) vs. Nb/Ta (by weight); (<b>b</b>), Nb vs. Ta by weight; (<b>c</b>), U vs. Th by weight; (<b>d</b>), Pb vs. Zn by weight. Data from Raimbault et al. [<a href="#B48-minerals-14-01302" class="html-bibr">48</a>] (Beauvoir), Badanina et al. [<a href="#B36-minerals-14-01302" class="html-bibr">36</a>] (Orlovka), and authors’ data (Madeira, Cínovec and Podlesí). Values for deeper crust from Rudnick and Gao [<a href="#B59-minerals-14-01302" class="html-bibr">59</a>].</p>
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<p>Back-scattered electron images (BSE) of pyrochlore crystals from the Madeira pluton. Fresh or only very slightly altered examples (type 1 pyrochlore): (<b>a</b>) an almost fresh homogeneous pyrochlore crystal associated with crystals of hematite (dark gray) in the cryolite-albite matrix (black), Madeira albite granite core facies (#PHR247, crystal 4); (<b>b</b>) a distinctly zoned pyrochlore crystal in darker zones starting to transform into columbite-Fe, Madeira albite granite core facies (#PHR 159, crystal 1); (<b>c</b>) a zoned pyrochlore crystal associated with zircon (dark gray) with overgrowths of columbite, Madeira albite granite core facies (#PHR 160, crystal 3); (<b>d</b>) a zoned pyrochlore crystal with overgrowths of columbite, Madeira albite granite core facies (#PHR 163, crystal 3). Type 2 pyrochlore: (<b>e</b>) an inhomogeneously zoned pyrochlore crystal with Pb-enriched (bright) domains and a thin veinlet of secondary columbite (dark), Madeira albite granite core facies (#PHR 242, crystal 7); (<b>f</b>) a distinctly zoned pyrochlore crystal starting to transform into columbite –Fe along cracks, Madeira albite granite core facies (#PHR 82A, crystal 7). Red numbers refer to EPMA analyses of pyrochlore (compare <a href="#minerals-14-01302-t001" class="html-table">Table 1</a>), and yellow numbers to analyses of columbite (compare <a href="#minerals-14-01302-t002" class="html-table">Table 2</a>). Scale bars in all cases 200 μm.</p>
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<p>Back-scattered electron images (BSE) of pyrochlore crystals from the Madeira pluton. Medium-grade altered examples (type 2 pyrochlore): (<b>a</b>) a zoned pyrochlore crystal with its core irregularly replaced with columbite along a network of thin cracks, Madeira albite granite core facies, (#PHR128, crystal 1); (<b>b</b>) zoned pyrochlore with the intermediate zone replaced with columbite, Madeira albite granite core facies, (#PHR160, crystal 1); (<b>c</b>) a zoned pyrochlore crystal with its core partly replaced with columbite and a thick columbite overgrowth. Bright domains are enriched in U. Madeira albite granite core facies (#PHR 163, crystal 2); (<b>d</b>) a zoned pyrochlore crystal with its core partly replaced with columbite and an altered rim enriched in Pb, associated with cassiterite. Madeira albite granite core facies (#PHR 245, crystal 6); (<b>e</b>) patchy-colored pyrochlore with the outer zone partly replaced with columbite, Madeira albite granite core facies (#PHR 128, crystal 3); (<b>f</b>) zoned pyrochlore replaced with columbite from the core and the rim, bright domains enriched in U or Pb, Madeira albite granite core facies (#PHR 245, crystal 1). Scale bars in all cases 200 μm.</p>
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<p>Back-scattered electron images (BSE) of pyrochlore crystals from the Madeira pluton. Strongly altered examples from the core albite granite (type 3 pyrochlore): (<b>a</b>) patchy-zoned pyrochlore replaced with columbite from the rim, Madeira albite granite core facies (#PHR128, crystal 2); (<b>b</b>) patchy-zoned pyrochlore irregularly replaced with columbite and rimmed by hematite, Madeira hypersolvus granite (#PHR191, crystal 1); (<b>c</b>) patchy-zoned pyrochlore irregularly replaced with columbite, Madeira albite granite core facies (#PHR171, crystal 4); (<b>d</b>) remnants of patchy-zoned pyrochlore replaced with hematite from the rims, Madeira albite granite core facies, (#PHR246, crystal 4); (<b>e</b>) remnants of strongly altered pyrochlore replaced with hematite, bright domains enriched in Pb, Madeira hypersolvus granite, (#PHR191, crystal 1); (<b>f</b>) a remnant of a euhedral pyrochlore crystal (bright area) replaced with columbite (dark) and uraninite (small bright inclusions), Madeira albite granite core facies (#PHR247, crystal 2). Scale bars in all cases 200 μm.</p>
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<p>Back-scattered electron images (BSE) of columbite from the Madeira border albite granite (sample PHR-174): (<b>a</b>) an aggregate of primary-looking tabular columbite crystals (gray) with small inclusions of cassiterite (bright); (<b>b</b>) an aggregate of tabular columbite crystals (gray) associated with pyrite (dark gray). Columbite is transformed to type 4 pyrochlore in two ways: (i) thin bright coatings of U-rich pyrochlore on the columbite surface and in the interstices, and (ii) pervasive replacement forming inhomogeneous colander-like domains of Si, U-rich pyrochlore with small bright spots of a U-rich phase. Scale bars 100 μm.</p>
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<p>Chemical characteristics of PSGM from the Madeira granite and some other rare-metal granites: (<b>a</b>) Nb vs. Ta; (<b>b</b>) Nb + Ta vs. Si; (<b>c</b>) F vs. Si; (<b>d</b>) Sn vs. W; (<b>e</b>) Ca vs. Na; (<b>f</b>) Th vs. U; (<b>g</b>) Pb vs. Na; (<b>h</b>) F vs. Na. All in atoms per formula unit (apfu).</p>
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<p>The distribution of REE in pyrochlore/microlite (chondrite-normalized according to [<a href="#B67-minerals-14-01302" class="html-bibr">67</a>]): (<b>a</b>) type 1 pyrochlore from the Madeira core albite granite: sample PHR160 in black, PHR161 in red; (<b>b</b>) type 2 pyrochlore from the Madeira core albite granite: sample PHR242 in black, PHR243 in red; (<b>c</b>) type 3 pyrochlore from the Madeira hypersolvus granite: sample PHR191, crystal 1 in black, crystal 2 in green; (<b>d</b>) type 3 pyrochlore from the Madeira core albite granite (sample PHR247 in black) and type 4 pyrochlore from the Madeira border albite granite (sample PHR174 in red); (<b>e</b>) microlite (in red) and pyrochlore (in black) from Cínovec.</p>
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<p>Chemical characteristics of CGM: (<b>a</b>) Mn/(Fe + Mn) vs. Ta/(Nb + Ta); (<b>b</b>) SnO<sub>2</sub> vs. WO<sub>3</sub>; (<b>c</b>) TiO<sub>2</sub> vs. UO<sub>2</sub>.</p>
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<p>The distribution of elements in a relatively fresh pyrochlore crystal from Madeira, sample PHR160, crystal 3. Relative contents of Si and Na perfectly show a thin cryolite halo immediately around pyrochlore, dividing it from albite, while the enrichment in Fe along crystal rims indicates columbite overgrowth/replacement. Scale bar equals 100 μm.</p>
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<p>The distribution of elements in a zoned pyrochlore crystal, sample PHR 82A, crystal 7: the distribution of Si and Na shows a cryolite halo separating pyrochlore from the feldspar matrix. A slight enrichment in Si indicates two zones of incipient alteration. The crystal is penetrated by a network of fissures along which it is replaced with columbite, as indicated by Fe enrichment. The behavior of U is similar to that of Pb but different from that of Th. Scale bar equals 250 μm.</p>
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<p>The distribution of elements in a strongly altered pyrochlore crystal, sample 247, crystal 2: the major part of the crystal is replaced with columbite-Fe. U, Pb-rich pyrochlore forms only small remnants at present, with lower Nb and Fe contents than in columbite. The major part of U and Th, primarily bound in pyrochlore and non-compatible in columbite, forms inclusions of thorite-coffinite s.s., while Pb was mostly dispersed. Scale bar equals 100 μm.</p>
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<p>Back-scattered electron images (BSE) of microlite and CGM from Orlovka deposit: (<b>a</b>) a fresh, zoned microlite crystal, a flat, banded pegmatite-aplite body (#O 353, crystal 10); (<b>b</b>) a zoned microlite crystal with a Nb-rich, slightly altered core and fresh, Ta-rich rims. The core is slightly altered along cracks and locally has a porous structure. Amazonite-topaz-lepidolite granite (#O-369, crystal 2); (<b>c</b>) an anhedral microlite grain altered from the rims inwards, amazonite-lepidolite granite (#O-253, grain 3); (<b>d</b>) a fresh, subhedral, zoned columbite-Mn crystal, fine-grained lepidolite granite (#4703, crystal 3); (<b>e</b>), a zoned crystal with an euhedral columbite-Mn core and anhedral tantalite-Fe rims, albite-muscovite granite (#O-222, crystal 1); (<b>f</b>) an anhedral grain of tantalite-Fe in association with wolframite, a flat, banded pegmatite-aplite body (#O-353, grain 7).</p>
Full article ">Figure 14
<p>Back-scattered electron images (BSE) of pyrochlore, microlite, and columbite from Cínovec: (<b>a</b>) microlite associated with pyrite, greisenized granite, Cínovec-South deposit (#5423, grain 1); (<b>b</b>) microlite replaced with cassiterite, greisenized granite, Cínovec-South deposit (#5436, grain 1); (<b>c</b>) an anhedral pyrochlore aggregate embedded in fluorite, Cínovec biotite granite, borehole CS-1, depth 741 m (#4690B, grain 1); (<b>d</b>) remnants of Si, U-rich pyrochlore and columbite, both replaced with scheelite, greisenized granite, Cínovec-South deposit (#5427, grain 2); (<b>e</b>) a zoned columbite crystal with two zones in the euhedral core and the patchy anhedral rim, quartz-zinnwaldite greisen, Cínovec-South deposit (#13, grain 2); (<b>f</b>) an aggregate of fine, tabular crystals of columbite, albite granite, Cínovec, borehole Cs-1, depth 24 m (#4972, grain 1).</p>
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<p>Occupancy of A and B sites in PSGM: (<b>a</b>), Na vs. Ca vs. other elements and vacancies at the A site; (<b>b</b>), Na + Ca vs. other elements vs. vacancies at the A site; (<b>c</b>), Nb vs. Ta vs. other elements at the B site. Data from Beauvoir, according to [<a href="#B10-minerals-14-01302" class="html-bibr">10</a>,<a href="#B49-minerals-14-01302" class="html-bibr">49</a>].</p>
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<p>Chemical characteristics of PSGM from different lithologies: (<b>a</b>) Nb vs. Ta; (<b>b</b>) Nb + Ta vs. Si; (<b>c</b>) F vs. Si; (<b>d</b>) Sn vs. W; (<b>e</b>) Ca vs. Na; (<b>f</b>) Th vs. U; (<b>g</b>) Pb vs. Na; (<b>h</b>) F vs. Na; all in atoms per formula unit (apfu). For data sources, see the Geology section.</p>
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12 pages, 12558 KiB  
Article
The Effects of Surface Plasma Carburization on the Microstructure and Molten Salt Corrosion Resistance of Ta
by Xuming Lv, Dongbo Wei, Xianpu Huang, Zeyu Gao and Pingze Zhang
Coatings 2024, 14(12), 1570; https://doi.org/10.3390/coatings14121570 - 16 Dec 2024
Viewed by 630
Abstract
In order to enhance the corrosion resistance of tantalum, the double-glow plasma (DGP) metallurgy technique was used to prepare TaC coatings on the tantalum. The morphology, microstructure, and phase constituents of TaC were examined by scanning electron microscopy (SEM) and X-ray diffraction (XRD). [...] Read more.
In order to enhance the corrosion resistance of tantalum, the double-glow plasma (DGP) metallurgy technique was used to prepare TaC coatings on the tantalum. The morphology, microstructure, and phase constituents of TaC were examined by scanning electron microscopy (SEM) and X-ray diffraction (XRD). Nano-indentation tests were used to evaluate the mechanical properties of the coatings. The specimens were immersed in NaCl-KCl molten salt at 830 °C to evaluate their corrosion resistance. The results showed that the coating prepared by the DGP technique has a thickness of approximately 5 µm, the diffusion layer has a thickness of 2.5 µm, and the nano-indentation hardness is measured to be 17.27 GPa. The high-temperature stable ceramic phase enhances the high-temperature oxidation resistance of pure tantalum (Ta), while the dense corroded surface and oxidation products improve the anti-corrosion property of TaC coatings. Full article
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<p>Schematic illustration of double-glow plasma surface carburizing technology producing TaC coatings on Ta surface.</p>
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<p>Surface SEM (<b>a</b>) and cross-section SEM (<b>c</b>) and XRD (<b>b</b>), EDS (<b>d</b>) analysis of carburization layer.</p>
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<p>Mechanical properties of the Ta matrix and TaC carburized coating layer. (<b>a</b>) Load-displacement curves; (<b>b</b>) nano-hardness and elastic modulus; (<b>c</b>) H/E and H<sup>3</sup>/E<sup>2</sup> ratios; (<b>d</b>) elastic work (W<sub>e</sub>), plastic work (W<sub>p</sub>), and their ratio (K).</p>
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<p>XRD pattern of Ta (<b>a</b>) and TaC (<b>b</b>) coatings after molten salt corrosion.</p>
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<p>Corrosion kinetics of TaC coatings and untreated Ta in NaCl-KCl melts.</p>
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<p>Surface morphologies of the Ta and TaC infiltration layers after molten salt corrosion. (<b>a</b>–<b>a2</b>) Ta 1 h, 4 h, 7 h; (<b>b</b>–<b>b2</b>) TaC 1 h, 4 h, 7 h.</p>
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<p>Cross-sectional morphology and elemental line scan of Ta matrix after molten salt corrosion for (<b>a</b>,<b>a1</b>) 1 h, (<b>b</b>,<b>b1</b>) 4 h, and (<b>c</b>,<b>c1</b>) 7 h, respectively. Cross-sectional morphology and elemental line scan of TaC infiltration layer after molten salt corrosion for (<b>d</b>,<b>d1</b>) 1 h, (<b>e</b>,<b>e1</b>) 4 h, and (<b>f</b>,<b>f1</b>) 7 h, respectively.</p>
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<p>Schematic illustration of corrosion behaviors of Ta and TaC coatings in NaCl-KCl molten salt.</p>
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14 pages, 21628 KiB  
Article
Oxidation Behavior and Creep Resistance of Cast MC-Strengthened CoNiFeMnCr HEAs at 1100 °C
by Patrice Berthod and Lionel Aranda
Micro 2024, 4(4), 751-764; https://doi.org/10.3390/micro4040046 - 3 Dec 2024
Viewed by 548
Abstract
The reinforcement of cast Cantor’s-type high-entropy alloys by MC carbides and their effect on the hot oxidation behavior were investigated. Three equimolar CoNiFeMnCr alloys without or with carbon and with either hafnium or tantalum were elaborated. Their as-cast microstructures were specified. Oxidation tests [...] Read more.
The reinforcement of cast Cantor’s-type high-entropy alloys by MC carbides and their effect on the hot oxidation behavior were investigated. Three equimolar CoNiFeMnCr alloys without or with carbon and with either hafnium or tantalum were elaborated. Their as-cast microstructures were specified. Oxidation tests were carried out in air at 1100 °C. Flexural creep tests were performed at 1100 °C at 10 MPa. The carbide-free CoNiFeMnCr alloy was single-phased. The version with Hf and C added and the one with Ta and C added contained interdendritic eutectic script HfC and TaC carbides, respectively. After oxidation for 50 h at 1100 °C, all alloys were covered by a (Cr,Mn)2O3 scale with various proportions of Cr and Mn. HfO2 or CrTaO4 also formed. Oxidation resulted in a deep depletion in Cr and in Mn in the subsurface. Oxidation is much faster for the three alloys by comparison with chromia-forming alloys. Their bad oxidation behavior is obviously due to Mn and protection by coating is to be considered. The creep deformation of the carbide-free CoNiFeMnCr alloy was very fast. The creep resistance of the two versions reinforced by either HfC or TaC deformed much slower. The addition of these MC carbides led to a deformation rate divided by five to ten times. Now, creep behavior comparisons with commercial alloys are to be conducted. They will be performed soon. Full article
(This article belongs to the Section Microscale Materials Science)
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<p>As-cast microstructure of the HEAbase alloy (SEM/BSE image and elemental mapping).</p>
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<p>As-cast microstructure of the HEAhfc alloy (SEM/BSE image and elemental mapping).</p>
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<p>As-cast microstructure of the HEAtac alloy (SEM/BSE image and elemental mapping).</p>
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<p>Diffractogram acquired of one of the oxidized surfaces of the HEAbase alloy.</p>
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<p>Diffractogram acquired of one of the oxidized surfaces of the HEAhfc alloy.</p>
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<p>Diffractogram acquired of one of the oxidized surfaces of the HEAtac alloy.</p>
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<p>Low magnification SEM/BSE micrographs giving general views of the oxidized surfaces, subsurfaces and bulks.</p>
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<p>High-magnification SEM/BSE micrographs giving detailed views of the oxidized surfaces and subsurfaces, with the results of EDS spot analysis identification of the oxides.</p>
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<p>Elemental EDS cards of the oxidized surface and subsurface in the case of HEAbase.</p>
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<p>Elemental EDS cards of the oxidized surface and subsurface in the case of HEAhfc.</p>
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<p>Elemental EDS cards of the oxidized surface and subsurface in the case of HEAtac.</p>
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<p>Deformation curve of the HEAbase alloy, superposed with the corresponding deformation rate evolution.</p>
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<p>Deformation curve of the HEAhfc alloy, superposed with the corresponding deformation rate evolution.</p>
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<p>Deformation curve of the HEAtac alloy, superposed with the corresponding deformation rate evolution.</p>
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11 pages, 2359 KiB  
Article
An Investigation of Oxides of Tantalum Produced by Pulsed Laser Ablation and Continuous Wave Laser Heating
by Alexander W. Auner, Jonathan C. Crowhurst, David G. Weisz, Zurong Dai and Kimberly B. Knight
Materials 2024, 17(20), 4947; https://doi.org/10.3390/ma17204947 - 10 Oct 2024
Viewed by 686
Abstract
Recent progress has seen multiple Ta2O5 polymorphs generated by different synthesis techniques. However, discrepancies arise when these polymorphs are produced in widely varying thermodynamic conditions and characterized using different techniques. This work aimed to characterize and compare Ta2O [...] Read more.
Recent progress has seen multiple Ta2O5 polymorphs generated by different synthesis techniques. However, discrepancies arise when these polymorphs are produced in widely varying thermodynamic conditions and characterized using different techniques. This work aimed to characterize and compare Ta2O5 particles formed at high and low temperatures using nanosecond pulsed laser ablation (PLA) and continuous wave (CW) laser heating of a local area of tantalum in either air or an 18O2 atmosphere. Scanning electron microscopy (SEM) and Raman spectroscopy of the micrometer-sized particles generated by PLA were consistent with either a localized amorphous Ta2O5 phase or a similar, but not identical, crystalline β-Ta2O5 phase. The Raman spectrum of the material formed at the point of CW laser impingement was in good agreement with the previously established ceramic “H-Ta2O5” phase. TEM and electron diffraction analysis of these particles indicated the phase structure matched an oxygen-vacated superstructure of monoclinic H-Ta2O5. Further from the point of laser impingement, CW heating produced particles with a Raman spectrum that matched β-Ta2O5. We confirmed that the high-temperature ceramic phase characterized in previous work by Raman spectroscopy was the same monoclinic phase characterized in different work by TEM and could be produced by direct laser heating of metal in air. Full article
(This article belongs to the Special Issue Advanced Laser Ablation and Damage in Materials)
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<p>Secondary electron SEM image of tantalum surface showing laser-induced damage and oxide formation in air in (<b>A</b>) 52° tilted stage image of CW heating with red and blue arrows indicating two regions of distinct particles on and outside the crater edge, respectively. (<b>B</b>) Higher-magnification image of the crater edge and (<b>C</b>) pulsed laser ablation edge of crater. (<b>D</b>) Centimeters away from the crater center.</p>
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<p>Raman spectra of crystalline particles corresponding to locations on the tantalum metal surface shown in <a href="#materials-17-04947-f001" class="html-fig">Figure 1</a>A,C (blue arrow) from CW and pulsed ablation, respectively. Particulates were formed in either air (solid traces) or <sup>18</sup>O<sub>2</sub> (dashed traces). Each spectrum’s intensity is normalized with the highest peak set to 1 and the lowest point to 0; spectra are offset along the vertical direction for clarity.</p>
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<p>Raman spectral comparison of fine particulates from pulsed laser ablation in air on NaCl substrate (red trace) to β-Ta<sub>2</sub>O<sub>5</sub> produced by CW heating in air on the tantalum surface (black trace). Spectra from both traces underwent polynomial baseline subtraction and were then normalized to maximum peak height.</p>
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<p>Raman spectra of particulates on the tantalum metal surface near the point of laser impingement after CW heating in either air (solid trace) or <sup>18</sup>O<sub>2</sub> (dashed trace).</p>
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<p>(<b>A</b>) Bright-field TEM image of a cross-section specimen prepared by focused ion beam lift out. Grain sizes across the cross-section are on the order of micrometers. (<b>B</b>) High-resolution TEM image projected along the zone axis [013] of the monoclinic Ta<sub>2</sub>O<sub>5</sub> phase with the scale of the strong structural modulation marked. (<b>C</b>) Selected area electron diffraction pattern of the zone axis [120] with [hkl] coordinates (inset).</p>
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11 pages, 6721 KiB  
Article
Synthesis and NEXAFS and XPS Characterization of Pyrochlore-Type Bi1.865Co1/2Fe1/2Ta2O9+Δ
by Nadezhda A. Zhuk, Sergey V. Nekipelov, Olga V. Petrova, Aleksandra V. Koroleva, Aleksey M. Lebedev and Boris A. Makeev
Chemistry 2024, 6(5), 1078-1088; https://doi.org/10.3390/chemistry6050062 - 19 Sep 2024
Viewed by 966
Abstract
A cubic pyrochlore with the composition Bi1.865Co1/2Fe1/2Ta2O9+Δ (space group Fd-3m, a = 10.5013(8) Å) was synthesized from oxide precursors using solid-phase reactions. These ceramics are characterized by a porous microstructure formed by randomly oriented [...] Read more.
A cubic pyrochlore with the composition Bi1.865Co1/2Fe1/2Ta2O9+Δ (space group Fd-3m, a = 10.5013(8) Å) was synthesized from oxide precursors using solid-phase reactions. These ceramics are characterized by a porous microstructure formed by randomly oriented grains of an elongated shape with a longitudinal size of 0.5–1 µm. The electronic state of cobalt and iron ions in oxide ceramics was studied by NEXAFS and XPS spectroscopy. The parameters of the XPS spectra of Bi4f, Bi5d, Ta4f, Co2p, and Fe2p ionization thresholds for a complex pyrochlore were compared with the parameters of the corresponding oxides of the transition elements. The energy position of the XPS-Ta4f and -Ta5p spectra is shifted towards lower energies compared to the binding energy in tantalum(V) oxide by 0.75 eV. According to XPS spectroscopy, bismuth and tantalum cations have the corresponding effective charge of +3 and +(5-δ). The NEXAFS-Fe2p spectrum of ceramics coincides with the spectrum of Fe2O3 in its main spectrum characteristics and indicates the content of iron ions in the oxide ceramics in the form of octahedral Fe(III) ions, and according to the character of the Co2p spectrum, cobalt ions are predominantly in the Co(II) state. Full article
(This article belongs to the Section Inorganic and Solid State Chemistry)
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<p>Unit cell of the A<sub>2</sub>B<sub>2</sub>O<sub>7</sub> pyrochlore (sp.gr. Fd-3m).</p>
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<p>X-ray diffraction powder patterns of Bi<sub>1.865</sub>Fe<sub>1/2</sub>Co<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub> and Bi<sub>2</sub>Fe<sub>1/2</sub>Co<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub>. * denotes the reflections of the impurity phase—bismuth orthotantalate.</p>
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<p>EDS spectrum and elemental maps of the Bi<sub>1.865</sub>Fe<sub>1/2</sub>Co<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub> samples.</p>
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<p>Microphotograph of the Bi<sub>1.865</sub>Fe<sub>1/2</sub>Co<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub> surface in the secondary and elastically reflected electron modes.</p>
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<p>Survey XPS spectrum of the Bi<sub>1.865</sub>Co<sub>1/2</sub>Fe<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub> (CoFe) (<b>a</b>); XPS-Bi4f spectra of Bi<sub>2</sub>O<sub>3</sub> and CoFe (<b>b</b>); XPS spectra of tantalum and bismuth cations in Bi<sub>2</sub>O<sub>3</sub>,Ta<sub>2</sub>O<sub>5</sub>, and CoFe (<b>c</b>); XPS-Co2p spectra of CoO, Co<sub>3</sub>O<sub>4</sub>, and CoFe (<b>d</b>); and XPS-Fe2p spectra of FeO, Fe<sub>2</sub>O<sub>3</sub>, and CoFe (<b>e</b>).</p>
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<p>NEXAFS-Fe2p (<b>a</b>) and -Co2p spectra (<b>b</b>) of the Bi<sub>1.865</sub>Co<sub>1/2</sub>Fe<sub>1/2</sub>Ta<sub>2</sub>O<sub>9+Δ</sub>.</p>
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18 pages, 11197 KiB  
Article
The Effects of Three Antibacterial Nanoparticle Coatings on the Surface Characteristics of Stainless Steel
by Ahmed Muhsin Yousif Al-Mayali, Ammar S. Kadhum and Thair L. Alzubaydi
Metals 2024, 14(8), 853; https://doi.org/10.3390/met14080853 - 25 Jul 2024
Viewed by 1062
Abstract
The aim of this study is to investigate the antibacterial capabilities of different coating durations of three nanoparticle (NP) coatings: molybdenum (Mo), tantalum (Ta), and zinc oxide (ZnO), and their effects on the surface characteristics of 316L stainless steel (SS). The coated substrates [...] Read more.
The aim of this study is to investigate the antibacterial capabilities of different coating durations of three nanoparticle (NP) coatings: molybdenum (Mo), tantalum (Ta), and zinc oxide (ZnO), and their effects on the surface characteristics of 316L stainless steel (SS). The coated substrates underwent characterization utilizing field emission scanning electron microscopy (FE-SEM), energy dispersive X-ray spectrometry (EDX), and X-ray diffractometer (XRD) techniques. The antibacterial efficacy of NPs was evaluated using the agar diffusion method. The FE-SEM and EDX images confirmed the presence of nano-sized particles of Mo, Ta, and ZnO on the surface of the substrates with perfectly symmetrical spheres and a uniform distribution of the NPs. All groups demonstrated antibacterial activity, and the ability to inhibit the growth of Streptococcus mutans and Lactobacillus acidophilus bacteria. The ZnO group had the most potent antibacterial effect, followed by the Mo group, while the Ta group had the least effect. A direct-current (DC) plasma sputtering system was used to produce nano-coatings of high purity that were homogeneous, crack-free and showed no sign of delamination. Bacterial strains exposed to Mo, Ta, and ZnO coated surfaces exhibited a significant loss of viability in a time-dependent manner. The optimum sputtering time to ensure the best antibacterial properties and preserve the resources was 1 hour (h) for Mo, 3 h for Ta and 6 h for ZnO. Full article
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<p>Distribution of the study samples. * The samples used for X-ray diffraction (XRD), field emission scanning electron microscopy (FE-SEM), and energy dispersive X-ray spectrometry (EDX) tests were also used for antibacterial tests.</p>
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<p>FE-SEM images for the coated stainless steel plate at low- and high-magnification powers: (<b>A</b>,<b>B</b>) Mo nanoparticles (NPs); (<b>C</b>,<b>D</b>) Ta NPs; and (<b>E</b>,<b>F</b>) ZnO NPs.</p>
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<p>The EDX for the examined SS plate showing the presence of Mo.</p>
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<p><b>The</b> EDX plot for the examined SS plate coated with Mo.</p>
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<p>The EDX for the examined SS plate showing the presence of Ta.</p>
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<p>The EDX plot for the examined SS plate coated with Ta.</p>
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<p>The EDX for the examined SS plate showing the presence of ZnO.</p>
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<p>The EDX plot for the examined SS plate coated with ZnO.</p>
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<p>X-ray diffraction pattern of the Ta NPs sputtering coating on the 316L SS substrate at different sputtering times.</p>
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<p>X-ray diffraction pattern of ZnO NPs sputtering coating on the 316L SS substrate at different sputtering times.</p>
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<p>XRD pattern of 316L stainless steel Mo coated using plasma sputtering under different sputtering time conditions.</p>
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<p>Shift in the peak position of the Mo XRD pattern.</p>
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<p>The inhibition zones of three different timing of Zinc oxide nanoparticles coatings against <span class="html-italic">S. mutans</span>: T1 (2 h): 1.4 cm, T2 (4 h): 1.6 cm, and T3 (6 h): 1.8 cm.</p>
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<p>The mean inhibition zones in the antibacterial test for Mo nanoparticles. T1, T2, and T3 represent 1, 2, and 3 hours of coating time.</p>
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<p>The mean inhibition zones in the antibacterial test for Ta nanoparticles. T1, T2, and T3 represent 1, 2, and 3 hours of coating time.</p>
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<p>The mean inhibition zones in the antibacterial test for ZnO nanoparticles. T1, T2 and T3 represent 2, 4, and 6 hours of coating time.</p>
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16 pages, 5833 KiB  
Article
Performance Enhancement of Ti/IrO2-Ta2O5 Anode through Introduction of Tantalum–Titanium Interlayer via Double-Glow Plasma Surface Alloying Technology
by Mingshuai Guo, Yueren Liu, Yonglei Xin, Likun Xu, Lili Xue, Tigang Duan, Rongrong Zhao, Junji Xuan and Li Li
Nanomaterials 2024, 14(14), 1219; https://doi.org/10.3390/nano14141219 - 18 Jul 2024
Viewed by 1175
Abstract
Ti/IrO2-Ta2O5 electrodes are extensively utilized in the electrochemical industries such as copper foil production, cathodic protection, and wastewater treatment. However, their performance degrades rapidly under high current densities and severe oxygen evolution conditions. To address this issue, we [...] Read more.
Ti/IrO2-Ta2O5 electrodes are extensively utilized in the electrochemical industries such as copper foil production, cathodic protection, and wastewater treatment. However, their performance degrades rapidly under high current densities and severe oxygen evolution conditions. To address this issue, we have developed a composite anode of Ti/Ta-Ti/IrO2-Ta2O5 with a Ta-Ti alloy interlayer deposited on a Ti substrate by double-glow plasma surface alloying, and the IrO2-Ta2O5 surface coating prepared by the traditional thermal decomposition method. This investigation indicates that the electrode with Ta-Ti alloy interlayer reduces the agglomerates of precipitated IrO2 nanoparticles and refines the grain size of IrO2, thereby increasing the number of active sites and enhancing the electrocatalytic activity. Accelerated lifetime tests demonstrate that the Ti/Ta-Ti/IrO2-Ta2O5 electrode exhibits a much higher stability than the Ti/IrO2-Ta2O5 electrode. The significant improvement in electrochemical stability is attributed to the Ta-Ti interlayer, which offers high corrosion resistance and effective protection for the titanium substrate. Full article
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<p>SEM morphologies of (<b>A</b>) Ti substrate after etching in hot oxalic acid, (<b>B</b>,<b>C</b>) Ta-Ti alloy interlayer deposited via DGPSAT. (<b>C</b>) is the enlarged photo of (<b>B</b>).</p>
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<p>Cross-sectional morphology of Ta-Ti interlayer (<b>A</b>) and elements distribution with depth of Ta-Ti interlayer (<b>B</b>). The green line with arrow in (<b>A</b>) represents the location for EDS analysis by line scanning.</p>
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<p>SEM morphologies (<b>A</b>–<b>D</b>) and EDS mapping (<b>E</b>,<b>F</b>) of Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> anode (<b>A</b>,<b>C</b>,<b>E</b>) and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> composite anode (<b>B</b>,<b>D</b>,<b>F</b>). (<b>E</b>,<b>F</b>) are EDS mappings of (<b>C</b>,<b>D</b>), respectively.</p>
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<p>XRD patterns of Ta-Ti interlayer (<b>A</b>) and Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes (<b>B</b>).</p>
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<p>XPS spectra of Ta-Ti interlayer before and after sputtering to a depth of 60 nm. (<b>A</b>) full spectrum, (<b>B</b>) Ta-4f and (<b>C</b>) O-1s.</p>
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<p>XPS spectra of Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes. (<b>A</b>) full spectrum, (<b>B</b>) Ir-4f, (<b>C</b>) Ta-4f, and (<b>D</b>) O-1s.</p>
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<p>(<b>A</b>) Linear sweep voltammetry curves of Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes measured in 0.5 mol·L<sup>−1</sup> H<sub>2</sub>SO<sub>4</sub> solution. (<b>B</b>) The overpotential for oxygen evolution of different electrodes at the current density of 10 mA·cm<sup>−2</sup>. (<b>C</b>) Tafel slopes of different electrodes.</p>
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<p>EIS spectra of Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes measured at 1.4 V vs. SCE in 0.5 mol·L<sup>−1</sup> H<sub>2</sub>SO<sub>4</sub> solution. (<b>A</b>) Nyquist plot and (<b>B</b>) Bode plot.</p>
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<p>(<b>A</b>,<b>B</b>) Cyclic voltammograms between 0.6 V and 0.8 V at different sweep rates for Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes, respectively. (<b>C</b>) Evolution of current density at 0.7 V vs. scan rate for different electrodes. (<b>D</b>) The relationship between voltammetric charge (<span class="html-italic">q</span><sup>∗</sup>) and the inverse square root of scanning rate (v<sup>−1/2</sup>) for different electrodes. (<b>E</b>) The relationship between the reciprocal voltammetric charge (<span class="html-italic">q</span><sup>∗</sup>)<sup>−1</sup> and square root of scanning rate (v<sup>1/2</sup>) for different electrodes.</p>
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<p>(<b>A</b>) Variation of cell voltage of Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> and Ti/Ta-Ti/IrO<sub>2</sub>-Ta<sub>2</sub>O<sub>5</sub> electrodes with time for the accelerated life testing at 3 A·cm<sup>−2</sup> in 1 mol·L<sup>−1</sup> H<sub>2</sub>SO<sub>4</sub> solution. (<b>B</b>) Potentiodynamic polarization curves of Ta-Ti interlayer and Ti substrate in 1 mol·L<sup>−1</sup> H<sub>2</sub>SO<sub>4</sub> solution.</p>
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14 pages, 1598 KiB  
Article
Surface Reduction of Li2CO3 on LLZTO Solid-State Electrolyte via Scalable Open-Air Plasma Treatment
by Mohammed Sahal, Jinzhao Guo, Candace K. Chan and Nicholas Rolston
Batteries 2024, 10(7), 249; https://doi.org/10.3390/batteries10070249 - 12 Jul 2024
Viewed by 2549
Abstract
We report on the use of an atmospheric pressure, open-air plasma treatment to remove Li2CO3 species from the surface of garnet-type tantalum-doped lithium lanthanum zirconium oxide (Li6.4La3Zr1.4Ta0.6O12, LLZTO) solid-state electrolyte [...] Read more.
We report on the use of an atmospheric pressure, open-air plasma treatment to remove Li2CO3 species from the surface of garnet-type tantalum-doped lithium lanthanum zirconium oxide (Li6.4La3Zr1.4Ta0.6O12, LLZTO) solid-state electrolyte pellets. The Li2CO3 layer, which we show forms on the surface of garnets within 3 min of exposure to ambient moisture and CO2, increases the interface (surface) resistance of LLZTO. The plasma treatment is carried out entirely in ambient and is enabled by use of a custom-built metal shroud that is placed around the plasma nozzle to prevent moisture and CO2 from reacting with the sample. After the plasma treatment, N2 compressed gas is flowed through the shroud to cool the sample and prevent atmospheric species from reacting with the LLZTO. We demonstrate that this approach is effective for removing the Li2CO3 from the surface of LLZTO. The surface chemistry is characterized with X-ray photoelectron spectroscopy to evaluate the effect of process parameters (plasma exposure time and shroud gas chemistry) on removal of the surface species. We also show that the open-air plasma treatment can significantly reduce the interface resistance. This platform demonstrates a path towards open-air processed solid-state batteries. Full article
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<p>Schematic of custom-built shroud enclosing the open-air plasma nozzle with shroud gas injection for cooling after plasma treatment while maintaining a locally inert environment.</p>
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<p>High-resolution XPS C 1s spectra of LLZTO pellet sample at three distinct instances: (<b>a</b>) initially following a two-day exposure of the LLZTO surface to ambient air, resulting in the formation of surface Li<sub>2</sub>CO<sub>3</sub>; (<b>b</b>) immediately after in situ Ar<sup>+</sup> sputtering in the XPS vacuum chamber was performed on the LLZTO surface to remove Li<sub>2</sub>CO<sub>3</sub>; and (<b>c</b>) after three minutes of exposure to ambient following Li<sub>2</sub>CO<sub>3</sub> removal by Ar<sup>+</sup> sputtering.</p>
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<p>C 1s spectra of the LLZTO surface captured before (on top) and after (on bottom) exposure to open-air plasma for varying durations: (<b>a</b>) 5 min, (<b>b</b>) 10 min, (<b>c</b>) 20 min, and (<b>d</b>) 40 min. Each treatment time was performed on a different pellet.</p>
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<p>Nyquist plot of the LLZTO pellet measured in a pouch cell observed after 2 days of ambient air exposure and after open-air plasma treatment for 20 min.</p>
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17 pages, 38110 KiB  
Article
Barrier Properties of Cr/Ta-Coated Zr-1Nb Alloy under High-Temperature Oxidation
by Maxim Sergeevich Syrtanov, Stepan Pavlovich Korneev, Egor Borisovich Kashkarov, Dmitrii Vladimirovich Sidelev, Evgeny Nikolaevich Moskvichev and Viktor Nikolaevich Kudiiarov
Metals 2024, 14(6), 645; https://doi.org/10.3390/met14060645 - 29 May 2024
Cited by 1 | Viewed by 1019
Abstract
In this paper, Cr (8 μm)/Ta (3 μm) bilayer coatings deposited on a Zr-1Nb alloy substrate were investigated and compared with a Cr-coated alloy under high-temperature steam oxidation at 1200–1400 °C. The bilayer coatings with α- and β-Ta interlayers were obtained by magnetron [...] Read more.
In this paper, Cr (8 μm)/Ta (3 μm) bilayer coatings deposited on a Zr-1Nb alloy substrate were investigated and compared with a Cr-coated alloy under high-temperature steam oxidation at 1200–1400 °C. The bilayer coatings with α- and β-Ta interlayers were obtained by magnetron sputtering. The Cr/Ta-coated samples were studied using scanning electron microscopy (SEM), X-ray diffraction (XRD), and optical microscopy (OM). The coating with an α-Ta interlayer can suppress the interdiffusion of chromium and zirconium more effectively up to 1330 °C in comparison with the coating having a β-Ta interlayer. The weight gain of the α-Ta-coated samples after oxidation at 1200 °C for 2000 s was 5–6 times lower than that of the Cr-coated Zr alloy samples. Oxidation at 1400 °C for 120 s showed no significant difference in the weight gain of the Cr- and Cr/Ta-coated Zr-1Nb alloy samples. It was shown that the effect of suppression of Zr-Cr interdiffusion by the barrier coating (α- and β-Ta) is only short-term. Full article
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<p>X-ray diffraction patterns of Zr-1Nb alloy samples with α- and β-Ta barrier interlayers.</p>
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<p>The SEM of Cr/Ta coatings before oxidation.</p>
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<p>Weight gains of Cr/α-Ta and Cr/β-Ta samples after high-temperature oxidation in steam at 1200 °C.</p>
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<p>Weight gains of Cr/α-Ta and Cr/β-Ta samples after high-temperature steam oxidation at 1250–1400 °C.</p>
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<p>SEM images and corresponding EDS maps of the Cr/Ta-coated Zr alloy samples after oxidation: (<b>a</b>) Cr/α-Ta at 1200 °C for 1000 s; (<b>b</b>) Cr/α-Ta at 1200 °C for 2000 s; (<b>c</b>) Cr/β-Ta at 1200 °C for 1000 s; (<b>d</b>) Cr/β-Ta at 1200 °C for 2000 s.</p>
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<p>SEM images and corresponding EDS maps of the Cr/Ta-coated Zr alloy samples after oxidation: (<b>a</b>) Cr/α-Ta at 1200 °C for 1000 s; (<b>b</b>) Cr/α-Ta at 1200 °C for 2000 s; (<b>c</b>) Cr/β-Ta at 1200 °C for 1000 s; (<b>d</b>) Cr/β-Ta at 1200 °C for 2000 s.</p>
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<p>SEM images and corresponding EDS maps of Cr/α-Ta samples after steam oxidation at different conditions: (<b>a</b>) 1250 °C and 120 s; (<b>b</b>) 1250 °C and 300 s; (<b>c</b>) 1330 °C and 120 s; (<b>d</b>) 1400 °C and 120 s.</p>
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<p>SEM images and corresponding EDS maps of Cr/α-Ta samples after steam oxidation at different conditions: (<b>a</b>) 1250 °C and 120 s; (<b>b</b>) 1250 °C and 300 s; (<b>c</b>) 1330 °C and 120 s; (<b>d</b>) 1400 °C and 120 s.</p>
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<p>SEM images and corresponding EDS maps of Cr/β-Ta samples after steam oxidation at different conditions: (<b>a</b>) 1250 °C and 120 s; (<b>b</b>) 1250 °C and 300 s; (<b>c</b>) 1330 °C and 120 s.</p>
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<p>Optical cross-sectional micrographs of the Cr/Ta-coated Zr alloy samples after oxidation: (<b>a</b>) Cr/α-Ta at 1200 °C for 1000 s; (<b>b</b>) Cr/α-Ta at 1200 °C for 2000 s; (<b>c</b>) Cr/β-Ta at 1200 °C for 1000 s; (<b>d</b>) Cr/β-Ta at 1200 °C for 2000 s.</p>
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<p>Cross-sectional optical micrographs of the Cr/α-Ta-coated Zr alloy samples after oxidation at (<b>a</b>) 1250 °C for 120 s; (<b>b</b>) 1250 °C for 300 s; (<b>c</b>) 1330° C for 120 s; (<b>d</b>) 1400 °C for 120 s.</p>
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<p>Cross-sectional optical micrographs of the Cr/β-Ta-coated Zr alloy samples after oxidation at (<b>a</b>) 1250 °C for 120 s; (<b>b</b>) 1250 °C 300 s; (<b>c</b>) 1330 °C 120 s.</p>
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<p>Diffraction patterns of Cr/Ta-coated zirconium alloy during linear heating from room temperature to 1250 °C.</p>
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<p>X-ray diffraction patterns of Cr/Ta-coated zirconium alloy during heating at 1250 °C.</p>
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11 pages, 5332 KiB  
Article
X-ray Induced Electric Currents in Anodized Ta2O5: Towards a Large-Area Thin-Film Sensor
by Davide Brivio, Matt Gagne, Erica Freund, Erno Sajo and Piotr Zygmanski
Sensors 2024, 24(8), 2544; https://doi.org/10.3390/s24082544 - 16 Apr 2024
Viewed by 1087
Abstract
Purpose: We investigated the characteristics of radiation-induced current in nano-porous pellet and thin-film anodized tantalum exposed to kVp X-ray beams. We aim at developing a large area (≫cm2) thin-film radiation sensor for medical, national security and space applications. Methods: Large area [...] Read more.
Purpose: We investigated the characteristics of radiation-induced current in nano-porous pellet and thin-film anodized tantalum exposed to kVp X-ray beams. We aim at developing a large area (≫cm2) thin-film radiation sensor for medical, national security and space applications. Methods: Large area (few cm2) micro-thin Ta foils were anodized and coated with a counter electrode made of conductive polymer. In addition, several types of commercial electrolytic porous tantalum capacitors were assembled and prepared for irradiation with kVp X-rays. We measured dark current (leakage) as well as transient radiation-induced currents as a function of external voltage bias. Results: Large transient currents (up to 50 nA) under X-ray irradiation (dose rate of about 3 cGy/s) were measured in Ta2O5 capacitors. Small nano-porous Ta and large-area flat Ta foil capacitors show similar current–voltage characteristic curve after accounting for different X-ray attenuation in capacitor geometry. The signal is larger for thicker capacitor oxide. A non-negligible signal for null external voltage bias is observed, which is explained by fast electron production in Ta foils. Conclusions: Anodized tantalum is a promising material for use in large-area, self-powered radiation sensors for X-ray detection and for energy harvesting. Full article
(This article belongs to the Section Electronic Sensors)
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<p>Ta capacitor types: (<b>A</b>) picture of a bare pellet of anodized nano-porous tantalum capacitor (NP-TaC); H<sub>p</sub>, L<sub>p</sub> and W<sub>p</sub> are the physical dimensions of the pellet. (<b>B</b>) large-area flat thin-film Ta capacitor (FTF-TaC) made by anodizing a 50 μm Ta foil; the thickness <span class="html-italic">d</span> of the Ta<sub>2</sub>O<sub>5</sub> was 170 nm; counter electrode is made of PEDOT conductive polymer. (<b>C</b>) Schematic of the experimental circuit for current–voltage measurements.</p>
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<p>DC dark leakage current IV-curves for different fractions of the working voltage <span class="html-italic">V<sub>W</sub></span> (after waiting time of 120 s) for various types of commercial nano-porous electrolytic tantalum capacitor (NP-TaC). The legend indicates, “capacitance value, <span class="html-italic">V<sub>W</sub></span>, counter electrode material”.</p>
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<p>1 μF, 10 V NP-TaC capacitor under irradiation with 120 kVp, 63 mA, 63 mAs at source-to-surface distance (SSD) of 57.5 cm, as a function of time (<b>a</b>) and for different fractions of the working voltage (<b>b</b>). In (<b>b</b>), the signal I(t) is averaged over the two X-ray pulses after subtraction of the dark current (leakage).</p>
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<p>(<b>a</b>) Signal as a function of the fraction <span class="html-italic">V</span>/<span class="html-italic">V<sub>W</sub></span> under irradiation with 120 kVp, 63 mA, 63 mAs at SSD = 57.5 cm, averaged over the two X-ray pulses after subtraction of the dark current (leakage) for several commercial NP-TaC capacitors. (<b>b</b>) Same data as in (<b>a</b>) but renormalized to the value at 0.9 <span class="html-italic">V</span>/<span class="html-italic">V<sub>W</sub></span> after subtraction of the internal built-in potential (<span class="html-italic">V</span> → <span class="html-italic">V</span> − <span class="html-italic">V</span><sub>0</sub>).</p>
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<p>Oxide thickness (<b>a</b>) and oxide volume (<b>b</b>) dependence of the signal under irradiation with 120 kVp, 63 mA, 63 mAs at SSD = 57.5 cm and with <span class="html-italic">V</span>/<span class="html-italic">V<sub>W</sub></span> = 0.7 applied on all capacitors. The active area is calculated using Equation (4), and the active volume by multiplying the oxide thickness by the active area. The red square represents the flat thin-film Ta capacitor (FTF-TaC) made by anodizing a 50 μm Ta foil at a formation voltage of <span class="html-italic">V<sub>f</sub></span> = 100 V (for FTF-TaC, the active area is the physical area).</p>
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<p>Flat Thin-Film tantalum foil (FTF-TaC) anodized at the formation voltage of <span class="html-italic">V<sub>f</sub></span> = 100 V. The area of the counter electrode was 0.28 cm<sup>2</sup>. Response to 120 kVp X-rays at SSD = 100 cm: (<b>a</b>) Signal as a function of time for 100 mA and different voltages applied; (<b>b</b>) current–voltage curve under irradiation; (<b>c</b>) signal as a function of time for 25 mA and different mAs at 0.9 <span class="html-italic">V</span>/<span class="html-italic">V<sub>W</sub></span>; (<b>d</b>) mA dependence for <span class="html-italic">V</span> = 0, 0.9 <span class="html-italic">V<sub>W</sub></span> (2–20 mA (dashed line) delivered in fluoroscopic mode, 25–200 mA (solid lines) in radiography mode).</p>
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14 pages, 6859 KiB  
Article
Effect of B2O3 and Basic Oxides on Network Structure and Chemical Stability of Borosilicate Glass
by Ming Lian, Tian Wang and Chong Wei
Ceramics 2024, 7(2), 516-529; https://doi.org/10.3390/ceramics7020034 - 15 Apr 2024
Cited by 3 | Viewed by 2145
Abstract
Glass properties play crucial roles in ensuring the safety and reliability of electronic packaging. However, challenges, such as thermal expansion and resistance to acid corrosion, pose long-term service difficulties. This study investigated the impact of the microstructure on acid resistance by adjusting the [...] Read more.
Glass properties play crucial roles in ensuring the safety and reliability of electronic packaging. However, challenges, such as thermal expansion and resistance to acid corrosion, pose long-term service difficulties. This study investigated the impact of the microstructure on acid resistance by adjusting the glass composition. A glass material with excellent acid resistance was obtained by achieving a similar coefficient of thermal expansion to tantalum; it exhibited a weight loss rate of less than 0.03% when submerged in 38% sulfuric acid at 85 °C for 200 h. Theoretically, this glass can be used to seal wet Ta electrolytic capacitors. Differential scanning calorimetry (DSC) was used to analyze the glass transition temperature and thermal stability of borosilicate glasses. X-ray diffractometry (XRD), scanning electron microscopy (SEM), and Raman spectroscopy were used to study the microstructure of the amorphous phase of the borosilicate glass, which revealed a close relationship between the degree of network phase separation in the borosilicate glass and the degree of polymerization (isomorphic polyhedron value, IP) of the glass matrix. The IP value decreased from 3.82 to 1.98 with an increasing degree of phase separation. Boron transitions from [BO4] to [BO3] within the glass network structure with increasing boron oxide content, which diminishes the availability of free oxygen provided by alkaline oxide, resulting in a lower acid resistance. Notably, the glass exhibited optimal acid resistance at boron trioxide and mixed alkaline oxide contents of 15% and 6%, respectively. Raman experiments revealed how the distributions of various bridging oxygen atoms (Qn) affect the structural phase separation of the glass network. Additionally, Raman spectroscopy revealed the depolymerization of Q4 into Q3, thereby promoting high-temperature phase separation and highlighting the unique advantages of Raman spectroscopy for phase recognition. Full article
(This article belongs to the Special Issue Advances in Ceramics, 2nd Edition)
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<p>XRD pattern of base glass.</p>
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<p>Glass transition temperature (<b>a</b>) and thermal expansion coefficient (<b>b</b>) of base glass.</p>
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<p>Micromorphologies of samples under light microscope after 4% HF solution etching for 60 s ((<b>A<sub>1</sub></b>–<b>A<sub>6</sub></b>) in order).</p>
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<p>SEM and EDS of borosilicate glass after 60 s by 4% HF etching solution (green area represents B element EDS).</p>
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<p>EDS of glass dendritic phase separation.</p>
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<p>Raman spectrum of base glass after peak fitting.</p>
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<p>The Raman spectra of the stretching vibration (700 cm<sup>−1</sup>–1200 cm<sup>−1</sup>) of borosilicate glass (A<sub>1</sub>–A<sub>6</sub>).</p>
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<p>Basic glass expansion coefficient curve and acid resistance weight loss rate curve.</p>
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<p>Network structure mechanism diagram of B<sub>2</sub>O<sub>3</sub>-reinforced borosilicate base glass.</p>
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<p>Raman spectrum at stretching vibration (700 cm<sup>−1</sup>–1200 cm<sup>−1</sup>) of A<sub>2</sub> base glass after peak separation and fitting.</p>
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<p>Percentage of Q<sub>n</sub> (n = 1,2,3,4) in bending vibration (<b>a</b>) and stretching vibration (<b>b</b>) of sample A<sub>1</sub>–A<sub>6</sub>.</p>
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10 pages, 1558 KiB  
Article
NEXAFS and XPS Studies of Co Doped Bismuth Magnesium Tantalate Pyrochlores
by Nadezhda A. Zhuk, Boris A. Makeev, Aleksandra V. Koroleva, Sergey V. Nekipelov and Olga V. Petrova
Chemistry 2024, 6(2), 323-332; https://doi.org/10.3390/chemistry6020018 - 3 Apr 2024
Cited by 1 | Viewed by 1652
Abstract
Co doped bismuth magnesium tantalate with a pyrochlore structure (sp. gr. Fd-3m) was synthesized for the first time using the standard ceramic method. Single phase Bi2Mg1−xCoxTa2O9 samples were found to be formed when x [...] Read more.
Co doped bismuth magnesium tantalate with a pyrochlore structure (sp. gr. Fd-3m) was synthesized for the first time using the standard ceramic method. Single phase Bi2Mg1−xCoxTa2O9 samples were found to be formed when x < 0.7 in the X-ray phase analysis. However, with a higher cobalt content in the samples, the impurity phase β-BiTaO4 (sp. gr. P-1) is detected, and its amount is proportional to the degree of cobalt doping. The formation of solid solutions is evidenced by a uniform increase in the unit cell parameter of the Co,Mg co doped bismuth tantalate phase with an increase in the content of cobalt ions in the samples from 10.5412(8) (x = 0.3) to 10.5499(8) Å (x = 0.7). The samples exhibit a porous microstructure consisting of chaotically oriented and partially fused elongated grains measuring 1–2 μm. The dependence of the ceramic grain size on the n(Mg)/n(Co) ratio was not determined. X-ray spectroscopy (ear dge X-ray bsorption ine tructure (NEXAFS) and X-ray photoelectron spectroscopy (XPS)) was used to study the charge state of ions in Bi2Mg1−xCoxTa2O9. The NEXAFS and XPS data showed that doping with cobalt and magnesium did not change the bismuth and tantalum oxidation states in pyrochlore; in particular, the ions maintained their oxidation states of Bi(+3), Mg(+2) and Ta(+5). The energy position of the peaks of the Ta4f-, Ta5p-, Ta4d spectra had a characteristic shift towards lower energies compared to the binding energy in pentavalent tantalum oxide Ta2O5. A shift towards lower energies is characteristic of a decrease in the effective positive charge; in particular, for the Ta4f and Ta4d spectra we presented, this energy shift was ΔE = 0.65 eV, and in the region of the Ta4d edge—0.55 eV. This in turn allowed for us to assume that tantalum atoms have the same effective charge +(5-δ). The oxidation state of cobalt ions was predominantly 2+ and partially 3+, according to NEXAFS spectroscopy data. Full article
(This article belongs to the Section Inorganic and Solid State Chemistry)
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<p>X-ray patterns of Bi<sub>2</sub>Mg<sub>1−x</sub>Co<sub>x</sub>Ta<sub>2</sub>O<sub>9</sub> samples at different values of the х(Co) index. Asterisks indicate phase reflections of BiTaO<sub>4</sub> in the X-ray diffraction pattern.</p>
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<p>SEM microphotographs of the Bi<sub>2</sub>Mg<sub>1−x</sub>Co<sub>x</sub>TaO<sub>9</sub> at х(Co) = 0.3–0.7.</p>
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<p>Survey (<b>a</b>), Bi 4f (<b>b</b>) and Ta 4f (<b>c</b>) XPS spectra of Bi<sub>2</sub>Mg<sub>0.5</sub>Co<sub>0.5</sub>Ta<sub>2</sub>O<sub>9</sub>, Bi<sub>2</sub>MgTa<sub>2</sub>O<sub>9,</sub> Bi<sub>2</sub>CoTa<sub>2</sub>O<sub>9</sub> and Ta<sub>2</sub>O<sub>5</sub> and Bi<sub>2</sub>O<sub>3</sub> oxides; Mg 1s (<b>d</b>), Ta 4d and Bi 5d (<b>e</b>); Co 2p XPS spectra of Bi<sub>2</sub>Mg<sub>0.5</sub>Co<sub>0.5</sub>Ta<sub>2</sub>O<sub>9</sub>, Bi<sub>2</sub>CoTa<sub>2</sub>O<sub>9</sub> and Co<sub>3</sub>O<sub>4</sub>, CoO oxides (<b>f</b>).</p>
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<p>NEXAFS Co2p spectra of Bi<sub>2</sub>Mg<sub>1−x</sub>Co<sub>x</sub>Ta<sub>2</sub>O<sub>9</sub> and cobalt oxides CoO and Co<sub>3</sub>O<sub>4</sub>.</p>
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