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Search Results (2,944)

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13 pages, 12554 KiB  
Article
Comparative In Vitro Study of Sol–Gel-Derived Bioactive Glasses Incorporated into Dentin Adhesives: Effects on Remineralization and Mechanical Properties of Dentin
by In-Seong Park, Hyun-Jung Kim, Jiyoung Kwon and Duck-Su Kim
J. Funct. Biomater. 2025, 16(1), 29; https://doi.org/10.3390/jfb16010029 - 16 Jan 2025
Abstract
To overcome limitations of dentin bonding due to collagen degradation at a bonded interface, incorporating bioactive glass (BAG) into dentin adhesives has been proposed to enhance remineralization and improve bonding durability. This study evaluated sol–gel-derived BAGs (BAG79, BAG87, BAG91, and BAG79F) and conventional [...] Read more.
To overcome limitations of dentin bonding due to collagen degradation at a bonded interface, incorporating bioactive glass (BAG) into dentin adhesives has been proposed to enhance remineralization and improve bonding durability. This study evaluated sol–gel-derived BAGs (BAG79, BAG87, BAG91, and BAG79F) and conventional melt-quenched BAG (BAG45) incorporated into dentin adhesive to assess their remineralization and mechanical properties. The BAGs were characterized by using field-emission scanning electron microscopy (FE-SEM) and transmission electron microscopy for surface morphology. The surface area was measured by the Brunauer–Emmett–Teller method. X-ray diffraction (XRD) analysis was performed to determine the crystalline structure of the BAGs. Adhesive surface analysis was performed after approximating each experimental dentin adhesive and demineralized dentin by using FE-SEM. The elastic modulus of the treated dentin was measured after BAG-containing dentin adhesive application. The sol–gel-derived BAGs exhibited larger surface areas (by 400–600 times) than conventional BAG, with BAG87 displaying the largest surface area. XRD analysis indicated more pronounced and rapid formation of hydroxyapatite in the sol–gel BAGs. Dentin with BAG87-containing adhesive exhibited the highest elastic modulus. The incorporation of sol–gel-derived BAGs, especially BAG87, into dentin adhesives enhances the remineralization and mechanical properties of adhesive–dentin interfaces. Full article
(This article belongs to the Section Dental Biomaterials)
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<p>Representative FE-SEM images of BAGs. (<b>A</b>) BAG45 with low magnification (×5,000); (<b>B</b>) BAG45, (<b>C</b>) BAG79, (<b>D</b>) BAG87, (<b>E</b>) BAG91, and (<b>F</b>) BAG79F with high magnification (×30,000).</p>
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<p>Representative TEM images of BAGs. (<b>A</b>) BAG45 with low magnification (×25,000); (<b>B</b>) BAG45, (<b>C</b>) BAG79, (<b>D</b>) BAG87, (<b>E</b>) BAG91, (<b>F</b>) and BAG79F with high magnification (×50,000).</p>
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<p>Representative XRD graphs of BAGs. (<b>A</b>) BAG45 (<b>B</b>) BAG79, (<b>C</b>) BAG87, (<b>D</b>) BAG91, and (<b>E</b>) BAG79F. After 7 days, BAG79, -87, and -91 exhibited 2–3 times more intense peaks at 29.5° compared with BAG45. After 14 days, BAG79, -87, and -91 also showed 2 times more intense peaks compared with BAG45 at 29.5° and 2–3 times at 45.5°.</p>
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<p>Representative FE-SEM images of adhesive surface. (<b>A</b>) Group DA; (<b>B</b>) DA45; (<b>C</b>) DA79; (<b>D</b>) DA87; (<b>E</b>) DA91; and (<b>F</b>) DA79F.</p>
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<p>Representative FE-SEM images of dentin surface. (<b>A</b>) Group DD, completely demineralized dentin as control; (<b>B</b>) DA; (<b>C</b>) DA45; (<b>D</b>) DA79; (<b>E</b>) DA87; (<b>F</b>) DA91; (<b>G</b>) DA79F. Low magnification (×5000) of the experimental groups shown in the upper row and high magnification (×50,000) of the groups shown in the lower row.</p>
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<p>Elastic modulus measurement of dentin after experimental adhesive application. Asterisk (*) means statistical significance (<span class="html-italic">p</span> &lt; 0.05).</p>
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11 pages, 1851 KiB  
Article
The Influence of Two Spinning Processes of T800 Grade Carbon Fibers on the Mechanical Properties of Thermoplastic Composite Material
by Xu Cui, Xuefeng Sun, Weiguo Su, Shuo Wang and Han Guo
Coatings 2025, 15(1), 90; https://doi.org/10.3390/coatings15010090 - 15 Jan 2025
Viewed by 240
Abstract
Two types of T800 grade carbon fibers, produced using distinct spinning processes, were utilized to fabricate thermoplastic prepregs via the hot melt method. These prepregs were subsequently employed to produce thermoplastic composites. A universal testing machine was used to assess the tensile, bending, [...] Read more.
Two types of T800 grade carbon fibers, produced using distinct spinning processes, were utilized to fabricate thermoplastic prepregs via the hot melt method. These prepregs were subsequently employed to produce thermoplastic composites. A universal testing machine was used to assess the tensile, bending, and interlaminar shear properties of the composites, evaluating the impact of the two different spinning processes on their mechanical characteristics. The experimental results indicate that the dry spray wet spinning carbon fiber (T800-DJWS) exhibits a smoother surface, more regular cross-section, and more uniform distribution compared to the wet spinning carbon fiber (T800-WS), enhancing the prepreg preparation via the hot melt method. The T800-DJWS/PAEK composite demonstrates a tensile strength that is 706 MPa higher than the T800-WS/PAEK composite, while the latter exhibits a bending modulus 31 GPa higher than the former. Full article
(This article belongs to the Special Issue Advances and Trends in Bio-Based Electrospun Nanofibers)
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<p>T800-WS/PAEK prepreg and T800-DJWS/PAEK prepreg.</p>
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<p>Composite curing preparation curve.</p>
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<p>(<b>a</b>) Flexural test model, (<b>b</b>) shear strength test model.</p>
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<p>SEM images of carbon fibers with surface sizing agent removed: (<b>a</b>) T800-DJWS, (<b>b</b>) T800-WS.</p>
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<p>Metallographic images of T800 grade fiber cross-sections prepared by two different processes.</p>
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<p>Electron microscopic images of T800-DJWS/PAEK prepreg and T800-WS/PAEK prepreg.</p>
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<p>Tensile properties of T800-DJWS/PAEK composites and T800-WS/PAEK composites.</p>
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<p>T800-DJWS/PAEK and T800-WS/PAEK composite samples that experienced tensile test failure.</p>
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<p>Flexural text results for T800-DJWS/PAEK and T800-WS/PAEK.</p>
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<p>Electron microscope images of morphology of cross-sections of specimens after bending property test failure.</p>
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<p>Shear strength test results for T800-DJWS/PAEK and T800-WS/PAEK.</p>
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<p>Interlayer shear sample cross-section failure SEM images (Fiber in green oval box, resin in red dashed rectangular box).</p>
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10 pages, 5495 KiB  
Article
Effect of Laser Selective Melting on the Microstructure and Properties of Martensitic Stainless Steel After Annealing Treatment
by Biao Zhou, Shuai Huang, Tianyuan Wang, Zijun Zhao and Bingqing Chen
Materials 2025, 18(2), 354; https://doi.org/10.3390/ma18020354 - 14 Jan 2025
Viewed by 262
Abstract
This work investigated the 0Cr16Ni5Mo1 stainless steel using laser selective melting (SLM) technology and explored the effect of the tempering temperature on the microstructure and properties. After the tempering treatment, the quenched martensite transformed from a metastable [...] Read more.
This work investigated the 0Cr16Ni5Mo1 stainless steel using laser selective melting (SLM) technology and explored the effect of the tempering temperature on the microstructure and properties. After the tempering treatment, the quenched martensite transformed from a metastable to steady state, and residual austenite was formed. The results indicated that the elongation of the transverse specimen showed an upward trend as the tempering temperature increased, while the elongation of the longitudinal specimen first increased and then decreased. The fracture mode was ductile. There was an obvious fiber, radial, and shear lip zone on the fracture surface of transverse specimens. When the tempering temperature was 650 °C, the shear lip area of the fracture surface was the largest. For longitudinal specimens, there was no obvious zoning on the fracture surface. Full article
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<p>SEM images of microstructure for high- and low-amplification specimens at different tempering temperatures: 500 °C, 550 °C, 600 °C, and 650 °C.</p>
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<p>EBSD images of microstructure and grain size for specimens at different tempering temperatures: 500 °C, 550 °C, 600 °C, and 650 °C.</p>
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<p>Stress–strain curves at different tempering temperatures and directions.</p>
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<p>Mechanical properties of samples at different tempering temperatures: (<b>a</b>) transverse yield strength and tensile strength; (<b>b</b>) transverse elongation and cross-sectional shrinkage rate; (<b>c</b>) longitudinal yield strength and tensile strength; (<b>d</b>) longitudinal elongation and reduction in area.</p>
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<p>Hardness of the <sub>0</sub>Cr<sub>16</sub>Ni<sub>5</sub>Mo<sub>1</sub> martensitic stainless steel in different directions.</p>
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<p>High- and low-amplification transverse and longitudinal fracture morphology of samples at different tempering temperatures: 500 °C, 550 °C, 600 °C, and 650 °C.</p>
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13 pages, 3674 KiB  
Article
Production, Characterization, and In Vitro Antifungal Evaluation of Itraconazole-Loaded Fibrous Sheets Prepared by Electrospinning with a Factorial Design
by Emőke-Margit Rédai, Orsolya Péterfi, Attila Levente Gergely, Enikő Barabás, Andrada Pintea, Paula Antonoaea, Robert-Alexandru Vlad, Nicoleta Todoran, Cornelia-Titiana Cotoi, Adriana Ciurba and Emese Sipos
Appl. Sci. 2025, 15(2), 710; https://doi.org/10.3390/app15020710 - 13 Jan 2025
Viewed by 393
Abstract
Itraconazole (ITZ) is a broad-spectrum triazole antifungal agent suitable for the treatment of superficial and systemic mycoses. This study aimed to formulate, characterize, and evaluate the in vitro antifungal performance of single-jet electrospun itraconazole-loaded polyvinylpyrrolidone-based fibers. Fibrous mats were prepared under the following [...] Read more.
Itraconazole (ITZ) is a broad-spectrum triazole antifungal agent suitable for the treatment of superficial and systemic mycoses. This study aimed to formulate, characterize, and evaluate the in vitro antifungal performance of single-jet electrospun itraconazole-loaded polyvinylpyrrolidone-based fibers. Fibrous mats were prepared under the following experimental conditions: 10, 12.5, and 15 cm needle–collector distance, 20 kV tension, and 1, 1.5, and 2 mL/hour flow rate. The fibers were characterized by SEM, DSC, FTIR, assays, disintegration tests, dissolution tests, and in vitro antifungal activity. Using a 22 factorial design, the effects of preparation variables on the characteristics of the fibrous sheets were described. The electrospinning process led to smooth-surfaced, randomly oriented, and bead-free fibers. The average fiber diameter ranged from 887 nm to 1175 nm. The scanning calorimetry of pure ITZ revealed a sharp endothermic melting point at a temperature of 170 °C, not present in the curves of the fibers. After 60 min, between 70 and 100% of ITZ was released. The antifungal assay revealed that the fibers inhibited the growth of Candida albicans and Candida parapyilosis. The obtained fiber mats prepared from the hydrophilic polymer presented almost instantaneous disintegration, with potential applications for rapid antifungal delivery in oral or topical pharmaceutical form. Full article
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<p>Chemical structures of itraconazole (<b>a</b>) and polyvinylpyrrolidone (<b>b</b>).</p>
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<p>SEM images at 5000× magnification of samples N1 to N7 and 500× magnification of sample N7.</p>
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<p>FTIR spectra (<b>a</b>) and DSC curves (<b>b</b>) of ITZ, physical mixture (PM), N1 and N2 fibers, and PVP.</p>
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<p>Comparative dissolution curves of the samples and pure ITZ.</p>
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<p>Inhibition zones for Candida albicans for samples (N1–N7), empty fibers (E), and dispersion of ITZ (D).</p>
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<p>Summary plot of the factorial design (<b>a</b>) and factors influencing disintegration, including (<b>b</b>) replicates, (<b>c</b>) summary of fit, (<b>d</b>) coefficients, and (<b>e</b>) residuals.</p>
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<p>Influence of factors on dissolved amounts of ITZ after 5 min ((<b>a</b>) replicates, (<b>b</b>) summary of fit, (<b>c</b>) coefficients, and (<b>d</b>) residuals) and fiber diameter ((<b>e</b>) replicates, (<b>f</b>) summary of fit, (<b>g</b>) coefficients, and (<b>h</b>) residuals).</p>
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22 pages, 8471 KiB  
Article
Metal Powder Production by Atomization of Free-Falling Melt Streams Using Pulsed Gaseous Shock and Detonation Waves
by Sergey M. Frolov, Vladislav S. Ivanov, Viktor S. Aksenov, Igor O. Shamshin, Fedor S. Frolov, Alan E. Zangiev, Tatiana I. Eyvazova, Vera Ya. Popkova, Maksim V. Grishin, Andrey K. Gatin and Tatiana V. Dudareva
J. Manuf. Mater. Process. 2025, 9(1), 20; https://doi.org/10.3390/jmmp9010020 - 10 Jan 2025
Viewed by 491
Abstract
A new method of producing metal powders for additive manufacturing by the atomization of free-falling melt streams using pulsed cross-flow gaseous shock or detonation waves is proposed. The method allows the control of shock/detonation wave intensity (from Mach number 4 to about 7), [...] Read more.
A new method of producing metal powders for additive manufacturing by the atomization of free-falling melt streams using pulsed cross-flow gaseous shock or detonation waves is proposed. The method allows the control of shock/detonation wave intensity (from Mach number 4 to about 7), as well as the composition and temperature of the detonation products by choosing proper fuels and oxidizers. The method is implemented in laboratory and industrial setups and preliminarily tested for melts of three materials, namely zinc, aluminum alloy AlMg5, and stainless steel AISI 304, possessing significantly different properties in terms of density, surface tension, and viscosity. Pulsed shock and detonation waves used for the atomization of free-falling melt streams are generated by the pulsed detonation gun (PDG) operating on the stoichiometric mixture of liquid hydrocarbon fuel and gaseous oxygen. The analysis of solidified particles and particle size distribution in the powder is studied by sifting on sieves, optical microscopy, laser diffraction wet dispersion method (WDM), and atomic force microscopy (AFM). The operation process is visualized by a video camera. The minimal size of the powders obtained by the method is shown to be as low as 0.1 to 1 μm, while the maximum size of particles exceeds 400–800 μm. The latter is explained by the deficit of energy in the shock-induced cross-flow for the complete atomization of the melt stream, in particular dense and thick (8 mm) streams of the stainless-steel melt. The mass share of particles with a fraction of 0–10 μm can be at least 20%. The shape of the particles of the finest fractions (0–30 and 30–70 μm) is close to spherical (zinc, aluminum) or perfectly spherical (stainless steel). The shape of particles of coarser fractions (70–140 μm and larger) is more irregular. Zinc and aluminum powders contain agglomerates in the form of particles with fine satellites. The content of agglomerates in stainless-steel powders is very low. In general, the preliminary experiments show that the proposed method for the production of finely dispersed metal powders demonstrates potential in terms of powder characteristics. Full article
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<p>Schematic (<b>a</b>) and photograph (<b>b</b>) of the laboratory setup.</p>
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<p>Samples of aluminum powder: (<b>a</b>) on separator trays and (<b>b</b>) after collection and drying.</p>
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<p>Example of IP records in a single operation cycle during PDG operation in the frequency mode.</p>
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<p>PMSDs of zinc powder particles in separator trays #1–#4 obtained by means of dry sifting on sieves on fractions 140–250, 70–140, 30–70, and 0–30 μm; sample mass 313.8 g.</p>
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<p>Results of microscopic and AFM examination of zinc powder fractions (<b>a</b>) 140–250 µm and (<b>b</b>,<b>c</b>) 0–30 µm.</p>
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<p>Zinc powder PSDs obtained by laser diffraction WDM for several particle fractions: (<b>a</b>) 0–30 µm, (<b>b</b>) 30–70 µm, and (<b>c</b>) 70–140 µm.</p>
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<p>PMSDs of aluminum powder particles in separator trays #1–#4 obtained by means of dry sifting on sieves on fractions 140–250, 70–140, 30–70, and 0–30 μm; sample mass 143.2 g.</p>
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<p>Results of microscopic and AFM examination of aluminum powder fractions (<b>a</b>) 140–800 µm and (<b>b</b>,<b>c</b>) 0–30 µm.</p>
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<p>Aluminum powder PSDs obtained by laser diffraction WDM for several particle fractions: (<b>a</b>) 0–30 µm, (<b>b</b>) 30–70 µm, and (<b>c</b>) 70–140 µm.</p>
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<p>Sequential video frames of the shock-induced atomization process of the free-falling stream of stainless-steel melt.</p>
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<p>PMSDs of stainless-steel powder particles obtained by means of dry sifting on sieves on fractions (<b>a</b>) &gt;1000, 800–1000, 400–800, 250–400, 140–250, 70–140, 30–70, and 0–30 μm; and on fractions (<b>b</b>) 140–250, 70–140, 30–70, and 0–30 μm; sample weight 84.4 g.</p>
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<p>Results of microscopic and AFM examination of stainless-steel powder obtained on sieves (<b>a</b>) 70–140 µm and (<b>b</b>,<b>c</b>) 0–30 µm.</p>
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<p>Stainless-steel powder PSDs obtained by laser diffraction WDM for several particle fractions: (<b>a</b>) 30–70 µm, (<b>b</b>) 70–140 µm, and (<b>c</b>) 140–250 µm.</p>
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<p>Comparison of PSDs obtained by laser diffraction WDM for aluminum and zinc powders of fraction 0–30 µm.</p>
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<p>Comparison of PSDs obtained by laser diffraction WDM for zinc, aluminum, and stainless-steel powders of fraction 30–70 µm.</p>
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15 pages, 6277 KiB  
Article
Impact of Ag Coating Thickness on the Electrochemical Behavior of Super Duplex Stainless Steel SAF2507 for Enhanced Li-Ion Battery Cases
by Hyeongho Jo, Jung-Woo Ok, Yoon-Seok Lee, Sanghun Lee, Yonghun Je, Shinho Kim, Seongjun Kim, Jinyong Park, Jonggi Hong, Taekyu Lee, Byung-Hyun Shin, Jang-Hee Yoon and Yangdo Kim
Crystals 2025, 15(1), 62; https://doi.org/10.3390/cryst15010062 - 9 Jan 2025
Viewed by 320
Abstract
Li-ion batteries are at risk of explosions caused by fires, primarily because of the high energy density of Li ions, which raises the temperature. Battery cases are typically made of plastic, aluminum, or SAF30400. Although plastic and aluminum aid weight reduction, their strength [...] Read more.
Li-ion batteries are at risk of explosions caused by fires, primarily because of the high energy density of Li ions, which raises the temperature. Battery cases are typically made of plastic, aluminum, or SAF30400. Although plastic and aluminum aid weight reduction, their strength and melting points are low. SAF30400 offers excellent strength and corrosion resistance but suffers from work hardening and low high-temperature strength at 700 °C. Additionally, Ni used for plating has a low current density of 25% international copper alloy standard (ICAS). SAF2507 is suitable for use as a Li-ion battery case material because of its excellent strength and corrosion resistance. However, the heterogeneous microstructure of SAF2507 after casting and processing decreases the corrosion resistance, so it requires solution heat treatment. To address these issues, in this study, SAF2507 (780 MPa, 30%) is solution heat-treated at 1100 °C after casting and coated with Ag (ICAS 108.4%) using physical vapor deposition (PVD). Ag is applied at five different thicknesses: 0.5, 1.0, 1.5, 2.0, and 2.5 μm. The surface conditions and electrochemical properties are then examined for each coating thickness. The results indicate that the PVD-coated surface forms a uniform Ag layer, with electrical conductivity increasing from 1.9% ICAS to 72.3% ICAS depending on the Ag coating thickness. This enhancement in conductivity can improve Li-ion battery safety on charge and use. This result is expected to aid the development of advanced Li-ion battery systems in the future. Full article
(This article belongs to the Special Issue Advances in Surface Modifications of Metallic Materials)
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<p>Schematic diagram of the preparation and analysis timeline of Ag-coated super duplex stainless steel SAF2507: (# α) casting for manufacturing (red arrow), (# β) solution annealing to achieve homogeneous grains (red arrow), (# γ) Ag coating applied via PVD in thicknesses ranging from 0.0 to 2.5 μm (blue arrow), and (# δ) analysis of electrochemical behavior (green arrow).</p>
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<p>FE-SEM images illustrating the manufacturing process of super duplex stainless steel SAF2507: (<b>a</b>) casting and (<b>b</b>) solution annealing at 1100 °C.</p>
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<p>Volume fractions of austenite and ferrite in super duplex stainless steel SAF2507 for various manufacturing processes.</p>
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<p>Surface images of Ag-coated super duplex stainless steel SAF2507 with varying Ag coating thicknesses for enhanced Li-ion battery case applications: (<b>a</b>) coating thickness = 0.0 μm (before coating), (<b>b</b>) coating thickness = 0.5 μm, (<b>c</b>) coating thickness = 1.0 μm, (<b>d</b>) coating thickness = 1.5 μm, (<b>e</b>) coating thickness = 2.0 μm, and (<b>f</b>) coating thickness = 2.5 μm.</p>
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<p>XRD patterns for SDSS SAF2507 with varying Ag coating thicknesses for enhanced Li-ion battery cases: (<b>a</b>) intensity from 0 to 250,000 and (<b>b</b>) intensity from 0 to 5000.</p>
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<p>XRD patterns for SDSS SAF2507 with varying Ag coating thicknesses for enhanced Li-ion battery cases: (<b>a</b>) intensity from 0 to 250,000 and (<b>b</b>) intensity from 0 to 5000.</p>
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<p>Surface roughness of Ag-coated super duplex stainless steel SAF2507 at varying coating thicknesses from 0 to 2.5 μm: (<b>a</b>) Ra (μm) and (<b>b</b>) roughness gap, defined as the difference between the maximum and minimum roughness (μm).</p>
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<p>GDS results illustrating the relationship between thickness (μm) and the concentration of major alloying elements (%) in SDSS SAF2507 with various Ag coating thicknesses, employed in enhanced Li-ion battery cases: (<b>a</b>) coating thickness = 0.0 μm (before coating), (<b>b</b>) coating thickness = 0.5 μm, (<b>c</b>) coating thickness = 1.0 μm, (<b>d</b>) coating thickness = 1.5 μm, (<b>e</b>) coating thickness = 2.0 μm, and (<b>f</b>) coating thickness = 2.5 μm.</p>
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<p>Electrical conductivity as a function of Ag coating thickness on SDSS SAF2507.</p>
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<p>Time (s) vs potential (V) curve, i.e., OCP curve for various Ag coating thicknesses on super duplex stainless steel SAF2507 in NaCl electrolyte solution of 3.5 wt.%.</p>
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<p>Potentiodynamic polarization curves displaying the relationship between potential (V) and current density (A/cm<sup>2</sup>) for SDSS SAF2507 with varying Ag coating thicknesses.</p>
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<p>Image depicting chloride ion attack on Ag-coated SDSS SAF2507 in an electrolyte solution.</p>
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22 pages, 6639 KiB  
Article
Experimental and Numerical Simulation Study of Ultrasonic Vibration Effect on Abrasive Grain Distribution and Movement Behavior in Laser Cladding Melt Pool for Abrasive Layer Fabrication
by Zixuan Wang, Ying Chen, Chuang Guan, Jiahui Du, Tianbiao Yu, Ji Zhao and Jun Zhao
Appl. Sci. 2025, 15(2), 582; https://doi.org/10.3390/app15020582 - 9 Jan 2025
Viewed by 316
Abstract
The ultrasonic vibration laser cladding method is a material-saving and green method to fabricate super abrasive structured grinding wheels. However, the mechanism of the ultrasonic vibration’s effect on the movement behavior of abrasive grains in the laser cladding process has not been clarified. [...] Read more.
The ultrasonic vibration laser cladding method is a material-saving and green method to fabricate super abrasive structured grinding wheels. However, the mechanism of the ultrasonic vibration’s effect on the movement behavior of abrasive grains in the laser cladding process has not been clarified. To address this, the impacts of ultrasonic vibration on the abrasive grain distribution and movement behavior were experimentally studied, and the numerical simulation method was introduced to simulate the ultrasonic vibration laser cladding process. A two-dimensional Gaussian cross-section heat source model was developed, and its energy density conformed to a Gaussian distribution in both space and time. The simulations of the temperature and fluid fields of the melt pool were carried out. The CBN abrasive grains in the melt pool were subjected to gravity, the buoyancy force, the drag force of the metal fluid, and the sonophoretic radiation force of the ultrasonic vibration. Based on them, the effects of ultrasonic vibration on the movement behaviors and trajectories of the CBN abrasive grains were analyzed. The influence of the ultrasonic amplitude on the distribution of abrasive grains was studied. The simulation results revealed that the abrasive grains could be uniformly distributed on the surface of the cladding layer during the ultrasonic vibration laser cladding process. Full article
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<p>The laser cladding system: (<b>a</b>) the experimental equipment; (<b>b</b>) the system diagram.</p>
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<p>The macro-morphology of the printing layer: (<b>a</b>) the metal bond; (<b>b</b>) the mixture of metal bond and CBN abrasive grains.</p>
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<p>The morphology of a single CBN abrasive: (<b>a</b>) three-dimensional; (<b>b</b>) profile of cross-section.</p>
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<p>The CBN abrasive grain distribution on the surface of the printing layer: (<b>a</b>) r = 0%; (<b>b</b>) r = 10%; (<b>c</b>) r = 20%; (<b>d</b>) r = 30%; (<b>e</b>) r = 40%; (<b>f</b>) r = 50%.</p>
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<p>The multiphysical field coupling flowchart.</p>
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<p>The thermophysical parameters of Cu-Sn19-Ti10 alloy: (<b>a</b>) specific heat capacity; (<b>b</b>) heat conductivity coefficient; (<b>c</b>) density; (<b>d</b>) The solid and liquid phase transformation.</p>
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<p>The boundary of the molten pool.</p>
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<p>The temperature field evolution of the molten pool: (<b>a</b>) t = 1 ms; (<b>b</b>) t = 30 ms; (<b>c</b>) t = 100 ms; (<b>d</b>) t = 240 ms.</p>
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<p>The velocity distribution within the melt pool.</p>
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<p>The velocity distribution of molten metal in the direction of the depth of the melt pool.</p>
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<p>The CBN abrasive grain movement at different moments without ultrasonic vibration: (<b>a</b>) the initial stage; (<b>b</b>) the movement stage; (<b>c</b>) the final stage.</p>
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<p>The CBN abrasive grain movement at different moments with ultrasonic vibration: (<b>a</b>) the initial stage; (<b>b</b>) the movement stage; (<b>c</b>) the final stage.</p>
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<p>The CBN abrasive grain arrangement under different amplitude vibrations: (<b>a</b>) A = 0 μm; (<b>b</b>) A = 10 μm; (<b>c</b>) A = 20 μm; (<b>d</b>) A = 30 μm; (<b>e</b>) A = 40 μm.</p>
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<p>The duration of the CBN abrasive grain movement under different ultrasonic vibration amplitudes.</p>
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<p>CBN abrasive grain movement trajectory: (<b>a</b>) without ultrasonic vibration; (<b>b</b>) with ultrasonic vibration.</p>
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22 pages, 6110 KiB  
Article
Air–Ice–Water Temperature and Radiation Transfer via Different Surface Coverings in Ice-Covered Qinghai Lake of the Tibetan Plateau
by Ruijia Niu, Lijuan Wen, Chan Wang, Hong Tang and Matti Leppäranta
Water 2025, 17(2), 142; https://doi.org/10.3390/w17020142 - 8 Jan 2025
Viewed by 348
Abstract
There are numerous lakes in the Tibetan Plateau (TP) that significantly impact regional climate and aquatic ecosystems, which often freeze seasonally owing to the high altitude. However, the special warming mechanisms of lake water under ice during the frozen period are poorly understood, [...] Read more.
There are numerous lakes in the Tibetan Plateau (TP) that significantly impact regional climate and aquatic ecosystems, which often freeze seasonally owing to the high altitude. However, the special warming mechanisms of lake water under ice during the frozen period are poorly understood, particularly in terms of solar radiation penetration through lake ice. The limited understanding of these processes has posed challenges to advancing lake models and improving the understanding of air–lake energy exchange during the ice-covered period. To address this, a field experiment was conducted at Qinghai Lake, the largest lake in China, in February 2022 to systematically examine thermal conditions and radiation transfer across air–ice–water interfaces. High-resolution remote sensing technologies (ultrasonic instrument and acoustic Doppler devices) were used to observe the lake surface changes, and MODIS imagery was also used to validate differences in lake surface conditions. Results showed that the water temperature under the ice warmed steadily before the ice melted. The observation period was divided into three stages based on surface condition: snow stage, sand stage, and bare ice stage. In the snow and sand stages, the lake water temperature was lower due to reduced solar radiation penetration caused by high surface reflectance (61% for 2 cm of snow) and strong absorption by 8 cm of sand (absorption-to-transmission ratio of 0.96). In contrast, during the bare ice stage, a low reflectance rate (17%) and medium absorption-to-transmission ratio (0.86) allowed 11% of solar radiation to penetrate the ice, reaching 11.70 W·m−2, which increased the water temperature across the under-ice layer, with an extinction coefficient for lake water of 0.39 (±0.03) m−1. Surface coverings also significantly influenced ice temperature. During the bare ice stage, the ice exhibited the lowest average temperature and the greatest diurnal variations. This was attributed to the highest daytime radiation absorption, as indicated by a light extinction coefficient of 5.36 (±0.17) m−1, combined with the absence of insulation properties at night. This study enhances understanding of the characteristics of water/ice temperature and air–ice–water solar radiation transfer through effects of different ice coverings (snow, sand, and ice) in Qinghai Lake and provides key optical radiation parameters and in situ observations for the refinement of TP lake models, especially in the ice-covered period. Full article
(This article belongs to the Special Issue Ice and Snow Properties and Their Applications)
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<p>(<b>a</b>) Overview of Qinghai Lake, with the observation location marked by a red pentagram. (<b>b</b>) Layout of the observational instrumentation. (<b>c</b>–<b>f</b>) Instrument setup, manual snow thickness measurements, and lake ice thickness measurements via drilling.</p>
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<p>(<b>a</b>,<b>c</b>) Daily and (<b>b</b>,<b>d</b>) diurnal variations in (<b>a</b>,<b>b</b>) temperature and (<b>c</b>,<b>d</b>) wind speed at Qinghai Lake in 6–24 February 2022. The shaded areas in (<b>a</b>,<b>c</b>) correspond to the standard stages of lake cover: blue for snow, green for sand, and yellow for bare ice. Panels (<b>b</b>,<b>d</b>) display stage-averaged data for each variable. Note: Consistent with this article’s approach, the color coding in panels (<b>a</b>,<b>c</b>) is applied across all figures to represent the three distinct stages of the lake’s cover.</p>
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<p>Terra/MODIS images during the stable freezing period of Qinghai Lake in 6–24 February 2022, along with snapshots from the automatic weather station during the snow, sand, and bare ice stages. Two images from the automatic weather station are provided for each stage. The MODIS images are shown daily, except for 20 February, which has been removed due to distortion. Red corresponds to Band 3 (459–479 nm), green corresponds to Band 6 (1628–1652 nm), and blue corresponds to Band 7 (2105–2155 nm). Red areas represent ice and snow, cyan represents exposed soil, and white indicates small liquid water droplets in clouds. The lake surface is covered by a stable frozen ice layer.</p>
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<p>High-precision ultrasonic measurements of lake ice surface distances and thicknesses. The (<b>top</b>) graph depicts the distance from the sub-ice ultrasonic sensor to the underside of the ice, referred to as ’Under-ice’. The (<b>middle</b>) graph illustrates the distance from the ice surface ultrasonic sensor to the ice surface (or covering surface, if present), referred to as ’Surface-ice’. The (<b>bottom</b>) graph presents the combined thickness of the ice and any covering, measured from the top to the bottom surface, referred to as ’Ice and covering’.</p>
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<p>Temporal profiles of water temperature at various depths: (<b>a</b>) 12-hourly smoothed temperatures at 0.4 m, 0.5 m, 6.7 m, 8.7 m, and 12.7 m depths in February 2022; (<b>b</b>) 12-hourly smoothed temperatures at a depth of 2.1 m from February to April 2023, with the shaded area indicating the ice-covered period.</p>
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<p>(<b>a</b>) Thirty-minute average lake ice temperature and (<b>b</b>) vertical temperature profile.</p>
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<p>(<b>a</b>,<b>c</b>) Long-term trends and (<b>b</b>,<b>d</b>) daily variations in (<b>a</b>,<b>b</b>) solar shortwave radiation and (<b>c</b>,<b>d</b>) albedo. The lines in (<b>a</b>) denote downward (blue), upward (green), and net (yellow) shortwave radiation The shaded areas in (<b>b</b>,<b>d</b>) correspond to the snow (blue), sand (green), and bare ice (yellow) periods.</p>
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<p>(<b>a</b>) Long-term trend and (<b>b</b>–<b>d</b>) daily variations in underwater radiation at depths of 0.7 m, 2.1 m, and the ice bottom.</p>
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<p>Temporal variation in the attenuation coefficients of the lake water (blue) and lake ice (yellow). Dots represent values at 10-minute intervals, and lines represent the daily average.</p>
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<p>(<b>a</b>) Long-term trend and (<b>b</b>) daily variation in lake ice transmittance.</p>
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<p>Schematic diagram depicting radiation transfer within the air–ice–water system of Qinghai Lake. The blue dashed box shows the absorption-to-transmission ratio.</p>
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16 pages, 8305 KiB  
Article
Investigating Fracture Behavior in Titanium Aluminides: Surface Roughness as an Indicator of Fracture Mechanisms in Ti-48Al-2Cr-2Nb Alloys
by Alessia Serena Perna, Lorenzo Savio, Michele Coppola and Fabio Scherillo
Metals 2025, 15(1), 49; https://doi.org/10.3390/met15010049 - 7 Jan 2025
Viewed by 335
Abstract
Titanium aluminides, particularly the Ti-48Al-2Cr-2Nb alloy, have drawn significant attention for their potential in high-temperature aerospace and automotive applications due to their exceptional performances and reduced density compared to nickel-based superalloys. However, their intermetallic nature poses challenges such as limited room-temperature ductility and [...] Read more.
Titanium aluminides, particularly the Ti-48Al-2Cr-2Nb alloy, have drawn significant attention for their potential in high-temperature aerospace and automotive applications due to their exceptional performances and reduced density compared to nickel-based superalloys. However, their intermetallic nature poses challenges such as limited room-temperature ductility and fracture toughness, limiting their widespread application. Additive manufacturing, specifically Electron Beam Melting (EBM), has emerged as a promising method for producing complex-shaped components of titanium aluminides, overcoming challenges associated with conventional production methods. This work investigates the fracture behavior of Ti-48Al-2Cr-2Nb specimens with different microstructures, including duplex and equiaxed, under tensile and high-cycle fatigue at elevated temperatures. Fracture surfaces were analyzed to distinguish between static and dynamic fracture modes. A novel method, employing confocal microscopy acquisitions, is proposed to correlate surface roughness parameters with the causes of failure, offering new insights into the fracture mechanisms of titanium aluminides. The results reveal significant differences in roughness values between the propagation and fracture zones for all the temperatures and microstructure tested. At 650 °C, the crack propagation zone exhibits lower Sq values than the fracture zone, with the fracture zone showing more pronounced roughness, particularly for the equiaxed microstructure. However, at 760 °C, the difference in Sq values between the propagation and fracture zones becomes more pronounced, with a more substantial increase in Sq values in the fracture zone. These findings contribute to understanding fracture behavior in titanium aluminides and provide a predictive framework for assessing structural integrity based on surface characteristics. Full article
(This article belongs to the Special Issue Research on Fatigue Behavior of Additively Manufactured Materials)
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<p>SEM images of the microstructure of specimens obtained via EBM technology and subjected to HIP treatment characterized by of (<b>a</b>) equiaxed microstructure (<b>b</b>) duplex microstructure.</p>
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<p>Stereomicroscope images of the specimens subjected to tensile tests characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxial microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Comparison of fracture surfaces at 500× magnification, following tensile testing for specimens characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxed microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Comparison of fracture surfaces at 1500× magnification, following tensile testing for specimens characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxed microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Confocal acquisition of fracture surfaces of specimens after tensile testing: (<b>a</b>) Waviness surface of a duplex specimen at 650 °C; (<b>b</b>) Roughness surface of a duplex specimen at 650 °C; (<b>c</b>) Waviness surface of a duplex specimen at 760 °C; (<b>d</b>) Roughness surface of a duplex specimen at 760 °C.</p>
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<p>Stereomicroscope images of the specimens subjected to HCF tests characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxed microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Comparison of fracture surfaces at 500× magnification, following HCF tests for specimens characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxed microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Comparison of fracture surfaces at 1500× magnification, following HCF tests for specimens characterized by: (<b>a</b>) duplex microstructure tested at 650 °C; (<b>b</b>) duplex microstructure tested at 760 °C; (<b>c</b>) equiaxed microstructure tested at 650 °C; (<b>d</b>) equiaxed microstructure tested at 760 °C.</p>
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<p>Confocal acquisition of fracture surfaces of specimens after HCF testing: (<b>a</b>) Waviness surface of a duplex specimen at 650 °C; (<b>b</b>) Roughness surface of a duplex specimen at 650 °C; (<b>c</b>) Waviness surface of a duplex specimen at 760 °C; (<b>d</b>) Roughness surface of a duplex specimen at 760 °C.</p>
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<p>Comparison of surface roughness values (Sq) for the propagation and fracture zones of specimens tested for HCF at 650 °C and 760 °C: (<b>a</b>) specimens with a duplex microstructure; (<b>b</b>) specimens with an equiaxed microstructure.</p>
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17 pages, 3681 KiB  
Article
Exploring Surface-Driven Mechanisms for Low-Temperature Sintering of Nanoscale Copper
by Jingyan Li, Zixian Song, Zhichao Liu, Xianli Xie, Penghui Guan and Yiying Zhu
Appl. Sci. 2025, 15(1), 476; https://doi.org/10.3390/app15010476 - 6 Jan 2025
Viewed by 427
Abstract
As the density of electronic packaging continues to rise, traditional soldering techniques encounter significant challenges, leading to copper–copper direct bonding as a new high-density connection method. The high melting point of copper presents difficulties for direct diffusion bonding under standard conditions, thus making [...] Read more.
As the density of electronic packaging continues to rise, traditional soldering techniques encounter significant challenges, leading to copper–copper direct bonding as a new high-density connection method. The high melting point of copper presents difficulties for direct diffusion bonding under standard conditions, thus making low-temperature copper–copper bonding a focal point of research. In this study, we examine the sintering process at various temperatures by constructing models with multiple nanoparticles and sintering them under different conditions. Our findings indicate that 600 K is a crucial temperature for direct copper–copper sintering. Below this threshold, sintering predominantly depends on structural adjustments driven by residual stresses and particle contact. Conversely, at temperatures of 600 K and above, the activation of rapid surface atomic motion enables further structural adjustments between nanoparticles, leading to a marked decrease in porosity. Mechanical testing of the sintered samples corroborated the structural changes at different temperatures, demonstrating that the surface dynamic motion of atoms inherent in low-temperature sintering mechanisms significantly affects the mechanical properties of nanomaterials. These findings have important implications for developing high-performance materials that align with the evolving requirements of modern electronic devices. Full article
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<p>Schematic diagram of the system modeling process and the sintering simulation process.</p>
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<p>The variations in average atomic kinetic energy and atomic potential energy throughout the entire sintering process at 600 K.</p>
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<p>(<b>a</b>) The difference in total energy of the system before and after sintering at different sintering temperatures. (<b>b</b>) The morphology and crystal phase distribution of the sintered samples were obtained at sintering temperatures of 300 K, 600 K, and 900 K. The green represents the FCC phase, the red indicates the slipped FCC phase, and the white denotes the amorphous phase.</p>
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<p>The pore volume and internal surface area of sintered samples are obtained at different sintering temperatures. The illustration depicts the method of extracting the internal surface of the sample sintered at a temperature of 500 K.</p>
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<p>The graph illustrating the relationship between the number of atomic jumps and the sintering temperature highlights the step occurring between 500 and 600 K with a red dashed line.</p>
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<p>(<b>a</b>–<b>f</b>) The distribution of jumping atoms within the sintering system from 0.1 ns to 2.0 ns. (<b>g</b>) The pore volume and (<b>h</b>) the internal surface area changes with time during the sintering.</p>
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<p>(<b>a</b>) The circular atomic motion occurring around the connected regions that are about to merge. (<b>b</b>) The percentage of FCC structure and the post-slip structure relative to the total number of atoms in samples formed at the same sintering temperature.</p>
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<p>(<b>a</b>) The bulk modulus and shear modulus of samples obtained at different sintering temperatures. (<b>b</b>) Schematic diagram illustrating the morphological changes in the system during the determination of bulk modulus and shear modulus.</p>
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<p>(<b>a</b>) The stress–strain relationship of sintered samples obtained at different sintering temperatures during uniaxial tensile testing. (<b>b</b>) The Young’s modulus measured from the slope of the stress–strain curve in the strain phase of less than 1%.</p>
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<p>The atomic shear strain during the stretching processes at 300 K, 600 K, and 900 K is presented. The corresponding simulation steps are indicated beneath each strain cloud diagram. The red arrows in the figure highlight the initial locations of structural failure.</p>
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24 pages, 8540 KiB  
Article
Numerical Simulation of Free Surface Deformation and Melt Stirring in Induction Melting Using ALE and Level Set Methods
by Pablo Garcia-Michelena, Emilio Ruiz-Reina, Olaia Gordo-Burgoa, Nuria Herrero-Dorca and Xabier Chamorro
Materials 2025, 18(1), 199; https://doi.org/10.3390/ma18010199 - 5 Jan 2025
Viewed by 532
Abstract
This study investigates fixed and moving mesh methodologies for modeling liquid metal–free surface deformation during the induction melting process. The numerical method employs robust coupling of magnetic fields with the hydrodynamics of the turbulent stirring of liquid metal. Free surface tracking is implemented [...] Read more.
This study investigates fixed and moving mesh methodologies for modeling liquid metal–free surface deformation during the induction melting process. The numerical method employs robust coupling of magnetic fields with the hydrodynamics of the turbulent stirring of liquid metal. Free surface tracking is implemented using the fixed mesh level set (LS) and the moving mesh arbitrary Lagrangian–Eulerian (ALE) formulation. The model’s geometry and operating parameters are designed to replicate a semi-industrial induction melting furnace. Six case studies are analyzed under varying melt masses and coil power levels, with validation performed by comparing experimentally measured free surface profiles and magnetic field distributions. The melt’s stirring velocity and recirculation patterns are also examined. The comparative analysis determines an improved performance of the ALE method, convergence, and computational efficiency. Experimental validation confirms that the ALE method reproduces the free surface shape more precisely, avoiding unrealistic topological changes observed in LS simulations. The ALE method faces numerical convergence difficulties for high-power and low-mass filling cases due to mesh element distortion. The proposed ALE-based simulation procedure is a potential numerical optimization tool for enhancing induction melting processes, offering scalable and robust solutions for industrial applications. Full article
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<p>(<b>a</b>) Semi-industrial induction melting furnace. (<b>b</b>) Depiction of model geometry and domains.</p>
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<p>(<b>a</b>) Model domains and boundaries. (<b>b</b>) Initial mesh representation.</p>
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<p>(<b>a</b>) Contact probes into the melt for free surface measurement. (<b>b</b>) Aluminum-wetted contact probes.</p>
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<p>Measured free surface profile for free surface shape measurement tests.</p>
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<p>Free surface oscillations and numerical coupling of magnetic fields and fluid dynamics.</p>
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<p>Comparison of magnetic field for simulation results and experimental measurement.</p>
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<p>Free surface profile simulation and experimental correlation for LS tracking at 25 kW power.</p>
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<p>Free surface profile simulation and experimental correlation for LS tracking at 40 kW power.</p>
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<p>LS simulation results for time steps of interest. (<b>a</b>) Multiphase flow. (<b>b</b>) Velocity field.</p>
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<p>Free surface profile simulation and experimental correlation for ALE at 25 kW power.</p>
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<p>Free surface profile simulation and experimental correlation for ALE at 40 kW power.</p>
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<p>(<b>a</b>) Mesh skewness for 5 kg and 25 kW. (<b>b</b>) Mesh refinement and near-wall curvature detail.</p>
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<p>Magnetic field, Lorentz force, and flow field for 5 kg and 10 kg at 25 kW power.</p>
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<p>Axial velocity (<math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="bold">u</mi> </mrow> <mrow> <mi mathvariant="bold">z</mi> </mrow> </msub> </mrow> </semantics></math>) in <math display="inline"><semantics> <mrow> <mi>r</mi> <mo>=</mo> <mn>0</mn> </mrow> </semantics></math> axis for the case studies.</p>
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16 pages, 5234 KiB  
Article
Detection and Attribution of a Spatial Heterogeneity in the Temporal Evolution of Bulgarian River Discharge
by Natalya A. Kilifarska, Gergana I. Metodieva and Antonia Ch. Mokreva
Geosciences 2025, 15(1), 12; https://doi.org/10.3390/geosciences15010012 - 5 Jan 2025
Viewed by 434
Abstract
The hydrosphere is an element of the climate system and changes in the latter are reasonably projected over the river outflow. Climatic changes, however, are unevenly distributed over the Earth, and understanding their regional imprint on the hydrosphere is of great importance. In [...] Read more.
The hydrosphere is an element of the climate system and changes in the latter are reasonably projected over the river outflow. Climatic changes, however, are unevenly distributed over the Earth, and understanding their regional imprint on the hydrosphere is of great importance. In this study, we have conducted a statistical analysis of the monthly maximum and minimum river discharge recorded in 22 hydrological stations located on 19 of the Bulgarian rivers during the period 1993–2022. We have found that in half of the river basins, the trend of the spring maximum discharge is significantly positive (α = 0.05). In the other half of the stations, the trend is neutral. The stations with a positive trend are not randomly distributed but grouped, forming a pattern crossing the country from northwest to southeast. This pattern of trend distribution raises questions about the causes of the irregular hydrological response to the rising global near-surface temperatures. A comparison of hydrological data with some climatic variables (i.e., temperature, precipitation, and ozone at 70 hPa), combined with neural network analysis results, suggests ozone as a possible reason for the heterogeneous hydrological response. Its effect could be explained by an imposed episodic warming of the near-surface temperature due to fluctuations in the ozone density near the tropopause, which in turn favours the faster melting of ice and snow in the corresponding river basins. Full article
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<p>Location of the Bulgarian river basins used in the current study, together with the hydrological stations measuring river discharge.</p>
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<p>Maps of river discharge trends: (<b>a</b>) maximum discharge (spring); (<b>b</b>) minimum discharge (autumn) on the territory of Bulgaria, calculated by linear regression. Values higher or lower than ±0.15 [m<sup>3</sup>/s/yr] are statistically significant at α = 0.05. Stars indicate the location of hydrological stations.</p>
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<p>Spatial distribution of the correlation between modelled and measured maximum streamflow as a function of total precipitation (<b>a</b>), temperature at 2 m above the surface (<b>b</b>) and ozone at 70 hPa (<b>c</b>). maximum streamflow trends (shown in <a href="#geosciences-15-00012-f002" class="html-fig">Figure 2</a>). Stars indicate the location of the hydrological stations.</p>
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<p>Maps of near-surface temperature (top) (<b>a</b>) and total precipitation (bottom) (<b>b</b>) dynamic anomalies calculated for the period 1993–2022 (coloured shading). The spring outflow trend, shown in <a href="#geosciences-15-00012-f002" class="html-fig">Figure 2</a>, is overlaid (contours). Stars indicate the location of hydrological stations.</p>
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<p>Maps of the spring near-surface temperature (<b>a</b>) and ozone at 70 hPa (<b>b</b>) dynamic anomalies, calculated for the period 1993–2022 (coloured shading). The red contours represents the spring outflow trend, shown in <a href="#geosciences-15-00012-f002" class="html-fig">Figure 2</a>. Stars indicate the location of hydrological stations.</p>
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<p>Schematic diagram of the effect of ozone on surface temperature and late winter/early spring river discharge; GhE stands for greenhouse effect.</p>
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<p>Maps of the autumn near-surface temperature (<b>a</b>) and ozone at 70 hPa (<b>b</b>) dynamic anomalies, calculated for the period 1993–2022 (coloured shading). Stars indicate the location of hydrological stations.</p>
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<p>Time series of the monthly discharge of the Maritsa River, measured in Plovdiv, and the ozone values at 70 hPa, over Plovdiv, for the period 1993–2022.</p>
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<p>Projection of the influence of ozone at 70 hPa on the rivers discharge, determined by an artificial neural network (colour shading). The green contours indicate the statistically significant trend in river discharge (shown in <a href="#geosciences-15-00012-f002" class="html-fig">Figure 2</a>). Stars indicate the location of hydrological stations.</p>
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16 pages, 3581 KiB  
Article
Greenhouse Gas Emissions from Molten Fluoride Electrolysis Composed of Raw and Magnet Recycling Derived Oxides: A Comparative Study
by Vesna S. Cvetković, Nataša M. Petrović, Laras Prasakti, Dominic Feldhaus, Srecko R. Stopic, Bernd Friedrich and Jovan N. Jovićević
Materials 2025, 18(1), 184; https://doi.org/10.3390/ma18010184 - 4 Jan 2025
Viewed by 450
Abstract
In situ measurements of the chemical identity and quantity of anode gases during electrochemical measurements and rare earth (RE) electrolysis from fluoride-based molten salts composed of different kinds of rare earth oxides (REOs) were performed using FTIR spectrometry. Linear sweep voltammetry (LSV) was [...] Read more.
In situ measurements of the chemical identity and quantity of anode gases during electrochemical measurements and rare earth (RE) electrolysis from fluoride-based molten salts composed of different kinds of rare earth oxides (REOs) were performed using FTIR spectrometry. Linear sweep voltammetry (LSV) was carried out to characterize oxidation processes and determine the anodic effect from NdF3 + PrF3 + LiF + REO melt. RE complex formation and subsequent reactions on the GC anode surface were discussed to understand the formation pathways of CO/CO2 and perfluorocarbon gases (PFC), mainly CF4 and C2F6. The LSV shows that increasing the REO content from 1 wt.% up to 4 wt.% in the system, leads to a positive shift in the critical potential for a full anode effect, recorded around 4.50 V vs. W with 4 wt.% REO. The FTIR results from on-line off-gas analysis during LSV measurements indicate that the anode gas products were composed mainly of CO and CO2, whereas CF4 can be detected before the full anode effect and C2F6 at and after this phenomenon. Compositions of off-gases from electrolysis performed using different kinds of REOs were compared. The main off-gas component was found to be CO in RE electrolysis with REOs as raw materials, while in electrolysis with magnet recycling derived oxides (MRDOs), CO2 content was slightly higher compared to CO. PFC emissions during RE electrolysis were generally similar: CF4 was detected periodically, but in negligible concentrations, while C2F6 was not detected. Full article
(This article belongs to the Special Issue Recycling and Sustainability of Industrial Solid Waste)
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<p>Schematic presentation of the experimental setup.</p>
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<p>The linear sweep voltammograms recorded on a glassy carbon electrode in the NdF<sub>3</sub> + PrF<sub>3</sub> + LiF +2 wt.% Pr<sub>6</sub>O<sub>11</sub> + 2 wt.%Nd<sub>2</sub>O<sub>3</sub> electrolyte at final potentials: (1) 4.00 V; (2) 5.00 V; and (3) 8.00 V vs. W; T = 1323 K.</p>
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<p>Off-gases recorded in situ with an FTIR spectrometer during LSV scan (anodic end potential 8.00 V, <a href="#materials-18-00184-f002" class="html-fig">Figure 2</a>) on GC electrode in NdF<sub>3</sub> + PrF<sub>3</sub> + LiF +2 wt.% Pr<sub>6</sub>O<sub>11</sub> + 2 wt.% Nd<sub>2</sub>O<sub>3</sub> electrolyte; T = 1323 K; (a) CO and CO<sub>2</sub>…(b) CF<sub>4</sub> and C<sub>2</sub>F<sub>6</sub> off-gases measured concentrations.</p>
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<p>Schematic presentation of the proposed reactions on GC anode, including COF<sub>2</sub> formation.</p>
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<p>Off-gases generated on the GC anode recorded in situ with an FTIR spectrometer during potentiostatic deposition at different potentials: −0.80 V and −0.90 V vs. W applied: (<b>a</b>) measurements for CO/CO<sub>2</sub> and (<b>b</b>) CF<sub>4</sub> off-gas; working electrode Mo, in NdF<sub>3</sub> + PrF<sub>3</sub> + LiF +2 wt.% Pr<sub>6</sub>O<sub>11</sub> + 2 wt.% Nd<sub>2</sub>O<sub>3</sub> electrolyte; T = 1323 K.</p>
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<p>Schematic flow diagram of magnet recycling-derived oxide (MRDO) production from end-of-life NdFeB magnet.</p>
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<p>The linear sweep voltammograms recorded on a GC electrode in the NdF<sub>3</sub> + PrF<sub>3</sub> + LiF electrolyte containing (<b>a</b>) 1 wt.% of MRDO; (<b>b</b>) 3 wt.% of MRDO; and (<b>c</b>) 4 wt.% MRDO at different end potentials, T = 1323 K.</p>
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<p>Off-gases generated on the GC anode recorded in situ with an FTIR spectrometer during LSV scans of <a href="#materials-18-00184-f007" class="html-fig">Figure 7</a>c anodic end potential 7.00 V vs. W, in NdF<sub>3</sub> + PrF<sub>3</sub> + LiF + 4 wt.% MRDO electrolyte; T = 1323 K; (<b>a</b>) CO and CO<sub>2</sub>…(<b>b</b>) CF<sub>4</sub> and C<sub>2</sub>F<sub>6</sub> off-gases concentrations measured.</p>
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<p>Off-gases generated on the GC anode recorded in situ with an FTIR spectrometer during potentiostatic deposition at potential of −0.90 V vs. W; working electrode Mo, in 64.41 wt.% NdF<sub>3</sub> + 21.37 wt.% PrF<sub>3</sub> + 12.5 wt.% LiF+ 4 wt.% MRDO electrolyte; T = 1323 K.</p>
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19 pages, 12502 KiB  
Article
Quantifying Spatiotemporal Changes in Supraglacial Debris Cover in Eastern Pamir from 1994 to 2024 Based on the Google Earth Engine
by Hehe Liu, Zhen Zhang, Shiyin Liu, Fuming Xie, Jing Ding, Guolong Li and Haoran Su
Remote Sens. 2025, 17(1), 144; https://doi.org/10.3390/rs17010144 - 3 Jan 2025
Viewed by 455
Abstract
Supraglacial debris cover considerably influences sub-debris ablation patterns and the surface morphology of glaciers by modulating the land–atmosphere energy exchange. Understanding its spatial distribution and temporal variations is crucial for analyzing melting processes and managing downstream disaster mitigation efforts. In recent years, the [...] Read more.
Supraglacial debris cover considerably influences sub-debris ablation patterns and the surface morphology of glaciers by modulating the land–atmosphere energy exchange. Understanding its spatial distribution and temporal variations is crucial for analyzing melting processes and managing downstream disaster mitigation efforts. In recent years, the overall slightly positive mass balance or stable state of eastern Pamir glaciers has been referred to as the “Pamir-Karakoram anomaly”. It is important to note that spatial heterogeneity in glacier change has drawn widespread research attention. However, research on the spatiotemporal changes in the debris cover in this region is completely nonexistent, which has led to an inadequate understanding of debris-covered glacier variations. To address this research gap, this study employed Landsat remote sensing images within the Google Earth Engine platform, leveraging the Random Forest algorithm to classify the supraglacial debris cover. The classification algorithm integrates spectral features from Landsat images and derived indices (NDVI, NDSI, NDWI, and BAND RATIO), supplemented by auxiliary factors such as slope and aspect. By extracting the supraglacial debris cover from 1994 to 2024, this study systematically analyzed the spatiotemporal variations and investigated the underlying drivers of debris cover changes from the perspective of mass conservation. By 2024, the area of supraglacial debris in eastern Pamir reached 258.08 ± 20.65 km2, accounting for 18.5 ± 1.55% of the total glacier area. It was observed that the Kungey Mountain region demonstrated the largest debris cover rate. Between 1994 and 2024, while the total glacier area decreased by −2.57 ± 0.70%, the debris-covered areas expanded upward at a rate of +1.64 ± 0.10% yr−1. The expansion of debris cover is driven by several factors in the context of global warming. The rising temperature resulted in permafrost degradation, slope destabilization, and intensified weathering on supply slopes, thereby augmenting the debris supply. Additionally, the steep supply slope in the study area facilitates the rapid deposition of collapsed debris onto glacier surfaces, with frequent avalanche events accelerating the mobilization of rock fragments. Full article
(This article belongs to the Special Issue Earth Observation of Glacier and Snow Cover Mapping in Cold Regions)
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<p>Schematic of debris sources (the ablation rate in the area above the boundary between supraglacial debris and bare ice is not constant but is shown to highlight the promoting effect of a thin debris cover on ablation).</p>
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<p>Overview of glacier and lake distribution in eastern Pamir (points with color represent sample sites selected by the 2024 RF classification model, and the decimal latitude and longitude coordinates of the points can be found in the <a href="#app1-remotesensing-17-00144" class="html-app">Supplementary Information</a>).</p>
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<p>Workflow schematic for the delineation of the supraglacial debris cover.</p>
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<p>Debris cover rate of glaciers in eastern Pamir (2024).</p>
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<p>Trends in debris cover and bare ice area in eastern Pamir from 1994 to 2024.</p>
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<p>Trends of changes in the debris cover area of typical glaciers from 1994 to 2024 (k represents the average rate of change in debris-covered areas; “debris variance high” indicates significant changes in the extent of debris cover in that area, while “low” indicates no change in the extent of debris cover).</p>
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<p>Spatial distribution of debris cover changes in eastern Pamir from 1994 to 2024.</p>
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<p>Proportion (%) of debris cover area changes under different (<b>a</b>) elevations and (<b>b</b>) slopes.</p>
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<p>Changes in debris cover area at different elevation gradients in the study area: (<b>a</b>) study area; (<b>b</b>) Kelayayilake glacier; (<b>c</b>) Qimugan glacier; (<b>d</b>) Kekesayi glacier.</p>
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<p>Glacier distribution map in the study area, showing 85 glaciers with data on the average debris supply slope (each point represents a glacier, with point colors indicating different average slope values).</p>
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<p>Comparison of 2000 RF classification results (red line) with RGI V7.0 (blue line) and CGI2 (green line): (<b>a</b>) Kekesayi glacier; (<b>b</b>) Qimugan glacier.</p>
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10 pages, 2775 KiB  
Proceeding Paper
Advancement of Electrospun Carbon Nanofiber Mats in Sensor Technology for Air Pollutant Detection
by Al Mamun, Mohamed Kiari, Abdelghani Benyoucef and Lilia Sabantina
Eng. Proc. 2024, 67(1), 82; https://doi.org/10.3390/engproc2024067082 - 3 Jan 2025
Viewed by 416
Abstract
The use of electrospun carbon nanofibers (ECNs) has been the focus of considerable interest due to their potential implementation in sensing. These ECNs have unique structural and morphological features such as high surface area-to-volume ratio, cross-linked pore structure, and good conductivity, making them [...] Read more.
The use of electrospun carbon nanofibers (ECNs) has been the focus of considerable interest due to their potential implementation in sensing. These ECNs have unique structural and morphological features such as high surface area-to-volume ratio, cross-linked pore structure, and good conductivity, making them well suited for sensing applications. Electrospinning technology, in which polymer solutions or melts are electrostatically deposited, enables the production of high-performance nanofibers with tailored properties, including fiber diameter, porosity, and composition. This controllability enables the use of ECNs to optimize sensing applications, resulting in improved sensor performance and sensitivity. While carbon nanofiber mats have potential for sensor applications, several challenges remain to improve selectivity, sensitivity, stability and scalability. Sensor technologies play a critical role in the global sharing of environmental data, facilitating collaboration to address transboundary pollution issues and fostering international cooperation to find solutions to common environmental challenges. The use of carbon nanofibers for the detection of air pollutants offers a variety of possibilities for industrial applications in different sectors, ranging from healthcare to materials science. For example, optical, piezoelectric and resistive ECNs sensors effectively monitor particulate matter, while chemoresistive and catalytic ECNs sensors are particularly good at detecting gaseous pollutants. For heavy metals, electrochemical ECNF sensors offer accurate and reliable detection. This brief review provides in-sights into the latest developments and findings in the fabrication, properties and applications of ECNs in the field of sensing. The efficient utilization of these resources holds significant potential for meeting the evolving needs of sensing technologies in various fields, with a particular focus on air pollutant detection. Full article
(This article belongs to the Proceedings of The 3rd International Electronic Conference on Processes)
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<p>(<b>a</b>) Atomic force microscopy (AFM) image of magnetic electrospun nanofiber mat. The scale bar shows 5 μm; (<b>b</b>) confocal laser scanning microscope (CLSM) image showing the PAN/gelatin nanofiber mats on a 3D-printed sample. The scale indicates 50 μm.</p>
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<p>Schematic of experimental setup for the fabrication of ZnO-MWCNT nanocomposite sensor and its ammonia gas sensing properties at room temperature. Reprinted from [<a href="#B56-engproc-67-00082" class="html-bibr">56</a>], with permission from Elsevier.</p>
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