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Keywords = plasma-based accelerator

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26 pages, 4387 KiB  
Article
Development and Testing of a Helicon Plasma Thruster Based on a Magnetically Enhanced Inductively Coupled Plasma Reactor Operating in a Multi-Mode Regime
by Anna-Maria Theodora Andreescu, Daniel Eugeniu Crunteanu, Maximilian Vlad Teodorescu, Simona Nicoleta Danescu, Alexandru Cancescu, Adrian Stoicescu and Alexandru Paraschiv
Appl. Sci. 2024, 14(18), 8308; https://doi.org/10.3390/app14188308 (registering DOI) - 14 Sep 2024
Viewed by 204
Abstract
A disruptive Electric Propulsion system is proposed for next-generation Low-Earth-Orbit (LEO) small satellite constellations, utilizing an RF-powered Helicon Plasma Thruster (HPT). This system is built around a Magnetically Enhanced Inductively Coupled Plasma (MEICP) reactor, which enables acceleration of quasi-neutral plasma through a magnetic [...] Read more.
A disruptive Electric Propulsion system is proposed for next-generation Low-Earth-Orbit (LEO) small satellite constellations, utilizing an RF-powered Helicon Plasma Thruster (HPT). This system is built around a Magnetically Enhanced Inductively Coupled Plasma (MEICP) reactor, which enables acceleration of quasi-neutral plasma through a magnetic nozzle. The MEICP reactor features an innovative design with a multi-dipole magnetic confinement system, generated by neodymium iron boron (NdFeB) permanent magnets, combined with an azimuthally asymmetric half-wavelength right (HWRH) antenna and a variable-section ionization chamber. The plasma reactor is followed by a solenoid-free magnetic nozzle (MN), which facilitates the formation of an ambipolar potential drop, enabling the conversion of electron thermal energy into ion beam energy. This study explores the impact of an inhomogeneous magnetic field on the heating mechanism of the HPT and highlights its multi-mode operation within a pulsed power range of 200 to 500 W of RF. The discharge state, characterized by high-energy electron-excited ions and low-energy excited neutral particles in the plasma plume, was analyzed using optical emission spectroscopy (OES). The experimental testing campaign, conducted under pulsed power excitation, reveals that, as RF input power increases, the MEICP reactor transitions from inductive (H-mode) to wave coupling (W-mode) discharge modes. Spectrograms, electron temperature, and plasma density measurements were obtained for the Helicon Plasma Thruster within its operational envelope. Based on OES data, the ideal specific impulse was estimated to exceed 1000 s, highlighting the significant potential of this technology for future LEO/VLEO space missions. Full article
13 pages, 4429 KiB  
Article
Photo-Thermal Conversion and Raman Sensing Properties of Three-Dimensional Gold Nanostructure
by Feng Shan, Jingyi Huang, Yanyan Zhu and Guohao Wei
Molecules 2024, 29(18), 4287; https://doi.org/10.3390/molecules29184287 - 10 Sep 2024
Viewed by 295
Abstract
Three-dimensional plasma nanostructures with high light–thermal conversion efficiency show the prospect of industrialization in various fields and have become a research hotspot in areas of light–heat utilization, solar energy capture, and so on. In this paper, a simple chemical synthesis method is proposed [...] Read more.
Three-dimensional plasma nanostructures with high light–thermal conversion efficiency show the prospect of industrialization in various fields and have become a research hotspot in areas of light–heat utilization, solar energy capture, and so on. In this paper, a simple chemical synthesis method is proposed to prepare gold nanoparticles, and the electrophoretic deposition method is used to assemble large-area three-dimensional gold nanostructures (3D-GNSs). The light–thermal water evaporation monitoring and surface-enhanced Raman scattering (SERS) measurements of 3D-GNSs were performed via theoretical simulation and experiments. We reveal the physical processes of local electric field optical enhancement and the light–thermal conversion of 3D-GNSs. The results show that with the help of the efficient optical trapping and super-hydrophilic surface properties of 3D-GNSs, they have a significant effect in accelerating water evaporation, which was increased by nearly eight times. At the same time, the three-dimensional SERS substrates based on gold nanosphere particles (GNSPs) and gold nanostar particles (GNSTs) had limited sensitivities of 10−10 M and 10−12 M to R6G molecules, respectively. Therefore, 3D-GNSs show strong competitiveness in the fields of solar-energy-induced water purification and the Raman trace detection of organic molecules. Full article
(This article belongs to the Special Issue Raman Spectroscopy Analysis of Surfaces)
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<p>(<b>a</b>) The absorption spectrum of the gold seed solution (inset: gold seed solution). (<b>b</b>) The TEM image of gold seed nanoparticles.</p>
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<p>SEM images of (<b>a</b>) GNSPs and (<b>b</b>) GNSTs. (<b>c</b>) Absorption spectra of GNSP and GNST solutions.</p>
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<p>Electric field distributions on the surface of (<b>a</b>) a single GNSP and (<b>b</b>) two GNSPs. (<b>c</b>) Electric field resonance spectra on the surface of a single GNSP and two GNSPs. Electric field distributions on the surface of (<b>d</b>) a single GNST and (<b>e</b>) two GNSTs. (<b>f</b>) Local electric field resonance spectra on the surface of a single GNST and two GNSTs.</p>
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<p>(<b>a</b>) Schematic illustration of the electrophoretic deposition method. (<b>b</b>) Experimental equipment used for assembling 3D-GNSs via electrophoretic deposition. (<b>c</b>) Physical picture of 3D-GNSs assembled via electrophoretic deposition.</p>
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<p>SEM images of (<b>a</b>) GNSP films and (<b>b</b>) GNST films. Images of the coupling effect within the electric field distribution for (<b>c</b>) GNSPs and (<b>d</b>) GNSTs. The insets in (<b>a</b>,<b>b</b>) are higher-magnification SEM images.</p>
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<p>(<b>a</b>) EDS spectrum of 3D-GNS. (<b>b</b>) Shape of water droplets on the surface of 3D-GNS. (<b>c</b>) Shape of water droplets on the surface of ITO glass. (<b>d</b>) Water drop contact angle on the 3D-GNS surface. (<b>e</b>) Water drop contact angle on the ITO glass surface. (<b>f</b>) Water droplet evaporation rate on the ITO glass and 3D-GNS surfaces.</p>
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<p>(<b>a</b>) Raman spectra of R6G molecules on 3D-GNS SERS substrate based on GNSPs. (<b>b</b>) Raman spectra of R6G molecules on 3D-GNS SERS substrate based on GNSTs.</p>
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<p>Schematic illustration of the synthesis of GNSTs.</p>
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21 pages, 44084 KiB  
Article
Self-Healing and Thermal Stability of LaMgAl11O19-Ti3AlC2 Composites for High-Temperature Abradable Applications
by Jingqi Huang, Wenbo Chen, Kaiyue Lü, Mingyi Xu, Longhui Deng, Jianing Jiang, Shujuan Dong, Meizhu Chen and Xueqiang Cao
Coatings 2024, 14(8), 938; https://doi.org/10.3390/coatings14080938 - 26 Jul 2024
Viewed by 602
Abstract
Defects such as interconnected pores and cracks can improve the abradability of ceramic-based abradable sealing coatings (ASCs) but may reduce the lifetime. Self-healing can potentially close cracks and transform interconnected pores into isolated ones through filling and sintering effects. Ti3AlC2 [...] Read more.
Defects such as interconnected pores and cracks can improve the abradability of ceramic-based abradable sealing coatings (ASCs) but may reduce the lifetime. Self-healing can potentially close cracks and transform interconnected pores into isolated ones through filling and sintering effects. Ti3AlC2 (TAC) was incorporated into LaMgAl11O19 (LMA) as both the self-healing agent and sintering aid, and plasma-sprayed LMA-based composite coatings were annealed at 1200 °C to assess their self-healing capabilities and then subjected to oxidation in air and corrosion in steam at 1300 °C to study their long-term stability. Results indicated that increasing TAC content significantly enhances self-healing effectiveness, evidenced by the closure of cracks and the isolation of pores. Oxidation and corrosion at 1300 °C led to significant grain growth and the formation of equiaxed grains with an aspect ratio of approximately 3, which may impair the toughening mechanism. Meanwhile, due to the preferential volatilization of Al in a steam environment, LTA decomposed into α-La2/3TiO3 and La4Ti3O12 phases, and the accelerated mass transfer also resulted in grain coarsening. Interestingly, the L20T composite coating with a porosity of 32.17 ± 0.94% and a hardness of 74.88 ± 1.55 HR15Y showed great potential for abradable applications due to its stable phase composition and uniform pore distribution. Full article
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<p>XRD patterns of the composite powders: (<b>a</b>) 2θ = 10–80° and (<b>b</b>) 2θ = 38–43°.</p>
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<p>(<b>a</b>,<b>b</b>) SEM and EDS results of the L20T composite powder.</p>
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<p>The preparation process and annealing of the free-standing composite coatings.</p>
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<p>XRD patterns of the composite coatings after annealing at 1200 °C: (<b>a</b>) 2θ = 10–80° and (<b>b</b>) 2θ = 25–35°.</p>
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<p>Surface SEM images of the composite coatings after annealing at 1200 °C: (<b>a</b>) L0T; (<b>b</b>) L5T; (<b>c</b>) L10T; (<b>d</b>) L20T.</p>
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<p>Cross-section SEM images of the composite coatings after annealing at 1200 °C: (<b>a</b>–<b>a″</b>) L0T; (<b>b</b>–<b>b″</b>) L5T; (<b>c</b>–<b>c″</b>) L10T; (<b>d</b>–<b>d″</b>) L20T.</p>
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<p>Porosity and density (<b>a</b>), hardness (<b>b</b>), crack ratio (<b>c</b>) and pore size distribution (<b>d</b>) of the composite coatings after annealing at 1200 °C. The red bars indicate porosity, and the green bars represent density in (<b>a</b>).</p>
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<p>Weight change of the composite coatings after air oxidation at 1300 °C.</p>
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<p>XRD patterns of the composite coatings after annealing at 1200 °C and air oxidation at 1300 °C: (<b>a</b>) L0T; (<b>b</b>) L5T; (<b>c</b>) L10T; (<b>d</b>) L20T. From bottom to top showing the samples subjected to 10 h annealing, 100 and 200 h air oxidation.</p>
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<p>La<sub>2</sub>O<sub>3</sub>-TiO<sub>2</sub>-Al<sub>2</sub>O<sub>3</sub> ternary phase diagram. Derived from [<a href="#B52-coatings-14-00938" class="html-bibr">52</a>,<a href="#B53-coatings-14-00938" class="html-bibr">53</a>].</p>
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<p>Surface SEM images of the composite coatings after (<b>a</b>–<b>d</b>) 100 h and (<b>a′</b>–<b>d′</b>) 200 h air oxidation at 1300 °C; (<b>a</b>,<b>a′</b>) L0T, (<b>b</b>,<b>b′</b>) L5T, (<b>c</b>,<b>c′</b>) L10T, (<b>d</b>,<b>d′</b>) L20T.</p>
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<p>Cross-section SEM images of the composite coatings after 200 h air oxidation at 1300 °C: (<b>a</b>–<b>a″</b>) L0T; (<b>b</b>–<b>b″</b>) L5T; (<b>c</b>–<b>c″</b>) L10T; (<b>d</b>–<b>d″</b>) L20T.</p>
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<p>Changes of porosity and density of the composite coatings after annealing at 1200 °C and air oxidation at 1300 °C. The red bars indicate porosity, and the green bars represent density.</p>
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<p>Weight change of the composite coatings after steam corrosion at 1300 °C.</p>
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<p>XRD patterns of the composite coatings after annealing at 1200 °C and steam corrosion at 1300 °C: (<b>a</b>) L0T; (<b>b</b>) L5T; (<b>c</b>) L10T; (<b>d</b>) L20T. From bottom to top showing the samples subjected to 10 h annealing, 100 and 200 h steam corrosion.</p>
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<p>Surface SEM images of the composite coatings after (<b>a</b>–<b>d</b>) 100 h and (<b>a′</b>–<b>d′</b>) 200 h steam corrosion at 1300 °C; (<b>a</b>,<b>a′</b>) L0T, (<b>b</b>,<b>b′</b>) L5T, (<b>c</b>,<b>c′</b>) L10T, (<b>d</b>,<b>d′</b>) L20T.</p>
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<p>Cross-section SEM images of the composite coatings after (<b>a</b>–<b>d</b>) 100 and (<b>a′</b>–<b>d″</b>) 200 h steam corrosion at 1300 °C; (<b>a</b>–<b>a″</b>) L0T, (<b>b</b>–<b>b″</b>) L5T, (<b>c</b>–<b>c″</b>) L10T, (<b>d</b>–<b>d″</b>) L20T.</p>
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<p>Changes of porosity and density of the composite coatings after annealing at 1200 °C and steam corrosion at 1300 °C. The red bars indicate porosity, and the green bars represent density.</p>
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33 pages, 2617 KiB  
Review
Profound Properties of Protein-Rich, Platelet-Rich Plasma Matrices as Novel, Multi-Purpose Biological Platforms in Tissue Repair, Regeneration, and Wound Healing
by Peter A. Everts, José Fábio Lana, Robert W. Alexander, Ignacio Dallo, Elizaveta Kon, Mary A. Ambach, André van Zundert and Luga Podesta
Int. J. Mol. Sci. 2024, 25(14), 7914; https://doi.org/10.3390/ijms25147914 - 19 Jul 2024
Viewed by 1747
Abstract
Autologous platelet-rich plasma (PRP) preparations are prepared at the point of care. Centrifugation cellular density separation sequesters a fresh unit of blood into three main fractions: a platelet-poor plasma (PPP) fraction, a stratum rich in platelets (platelet concentrate), and variable leukocyte bioformulation and [...] Read more.
Autologous platelet-rich plasma (PRP) preparations are prepared at the point of care. Centrifugation cellular density separation sequesters a fresh unit of blood into three main fractions: a platelet-poor plasma (PPP) fraction, a stratum rich in platelets (platelet concentrate), and variable leukocyte bioformulation and erythrocyte fractions. The employment of autologous platelet concentrates facilitates the biological potential to accelerate and support numerous cellular activities that can lead to tissue repair, tissue regeneration, wound healing, and, ultimately, functional and structural repair. Normally, after PRP preparation, the PPP fraction is discarded. One of the less well-known but equally important features of PPP is that particular growth factors (GFs) are not abundantly present in PRP, as they reside outside of the platelet alpha granules. Precisely, insulin-like growth factor-1 (IGF-1) and hepatocyte growth factor (HGF) are mainly present in the PPP fraction. In addition to their roles as angiogenesis activators, these plasma-based GFs are also known to inhibit inflammation and fibrosis, and they promote keratinocyte migration and support tissue repair and wound healing. Additionally, PPP is known for the presence of exosomes and other macrovesicles, exerting cell–cell communication and cell signaling. Newly developed ultrafiltration technologies incorporate PPP processing methods by eliminating, in a fast and efficient manner, plasma water, cytokines, molecules, and plasma proteins with a molecular mass (weight) less than the pore size of the fibers. Consequently, a viable and viscous protein concentrate of functional total proteins, like fibrinogen, albumin, and alpha-2-macroglobulin is created. Consolidating a small volume of high platelet concentrate with a small volume of highly concentrated protein-rich PPP creates a protein-rich, platelet-rich plasma (PR-PRP) biological preparation. After the activation of proteins, mainly fibrinogen, the PR-PRP matrix retains and facilitates interactions between invading resident cells, like macrophages, fibroblast, and mesenchymal stem cells (MSCs), as well as the embedded concentrated PRP cells and molecules. The administered PR-PRP biologic will ultimately undergo fibrinolysis, leading to a sustained release of concentrated cells and molecules that have been retained in the PR-PRP matrix until the matrix is dissolved. We will discuss the unique biological and tissue reparative and regenerative properties of the PR-PRP matrix. Full article
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<p>Portrayal of a 2-spin centrifugation method used to produce autologous PRP. PRP preparation involves the collection of a predetermined volume of peripheral blood in collection syringes containing an anticoagulant, like calcium citrate 3.8%. The predonated whole blood is gently loaded in a PRP device for gravitational cellular density separation using a two-spin centrifugation protocol. After the first spin cycle, the whole blood components are separated into three basic layers: the PPP suspension, the buffy coat demarcation layer, and the RBC layer. During the second centrifugation cycle, the platelet and other cells in the PPP fraction and RBC layer are further separated, resulting in a multicellular buffy coat stratum containing high concentrations of platelets and, eventually, leukocytes. A calculated portion of the PPP fraction is removed, leaving the platelet concentrate within a small volume of plasma for platelet resuspension. Thereafter, the PRP is extracted from the device. In this graphic, LR-PRP has been prepared, and the multicellular fractions consist of a high concentration of platelets, monocytes, lymphocytes, neutrophils, and some red blood cells. Abbreviations: PPP: platelet-poor plasma; RBC: red blood cells; LR-PRP: leukocyte-rich PRP; PRP: platelet-rich plasma.</p>
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<p>PR-PRP preparation. After the second spin, a calculated portion of the PPP fraction is removed with a syringe and attached with an empty syringe to the ultrafiltration device, as well as an effluent collection syringe, to collect the eliminated plasma water. The PPP syringes are manually pushed through the device, and plasma water, proteins smaller than 20 kDa, and cytokines are removed through the hollow fiber pores. After a series of passes, the PPP volume is significantly reduced, leading to a small and viscous volume of protein-rich plasma. The remaining PPP volume in the PRP device is used to resuspend the highly concentrated multicellular LR-PRP fraction and capture it from the PRP device. The concentrated protein-rich PPP and LR-PRP are consolidated into one syringe and gently mixed, creating PR-PRP. Abbreviations: LR-PRP: leukocyte-rich PRP; PPP: platelet-poor plasma; PRP: platelet-rich plasma; PR-PRP: protein-rich platelet concentrate. (the ultrafiltration device shown is the CORE™ Ultrafiltration System, developed by EmCyte Corporation<sup>®</sup>, Fort Myers, FL, USA).</p>
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<p>Visualization of PRF, LP-PR-PRP, and LR-PRP PR-PRP matrices. The PRF matrix and leukocyte-poor and leukocyte-rich PR-PRP matrices are exhibited. In a same-patient experiment, 130 mL of anticoagulated whole blood was extracted to prepare 10 mL of PRF, LP-PPR, and LR-PRP, using two 60 mL 2-spin PRP devices (PurePRP<sup>®</sup>SP, EmCyte Corporation<sup>®</sup>, Fort Myers, FL, USA). After the first spin, the PRF clot was removed from the test tube. After the 2nd spin of the LP and LR-PRP preparations, the PPP fraction was removed for ultrafiltration to concentrate the plasma to produce protein-rich PPP resuspended with the concentrated PRP fractions, described in detail in <a href="#ijms-25-07914-f002" class="html-fig">Figure 2</a>. Exactly 3 mL of both PRP formulations was consolidated with 3 mL of protein-rich PPP. To create the PR-PRP matrices, normal baseline clotting parameters were restored by adding 0.35 mL of NaCl 10% to the 6 mL PR-PRP volume. Thereafter, 150 IU of bovine thrombin was added to the re-calcified PR-PRP volume, mimicking the effect of TF for matrix formation.</p>
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<p>Schematic overview of the multistep physiological process of PR-PRP matrix creation and the sustained release of matrix biological components. The ultrafiltration device concentrates non-activated plasma proteins, including fibrinogen, consisting of two D-domains composed of α, β, γ chains, and plasma growth factors. After consolidating a small volume of high-concentration PRP with the concentrated protein suspension, fibrinogen undergoes a structural change in the presence of thrombin and calcium ions, leading to the cleavage of fibrinogen into FpA and FpB to form stable, complex, soluble fibrin monomers. The soluble monomer polymerizes to form half-staggered protofibrils. Several enzymes, including FXIIIa, and in presence of Ca<sup>++</sup> ions, protofibrils are converted to the cross-linked fibrin embedded with highly concentrated PRP cells. Fibrinolysis is initiated when t-PA converts plasminogen into plasmin, whereas PAI-1 inhibits t-PA, preventing the activation of plasminogen and thus fibrinolysis. Hence, FDP, D-dimers, platelets, and other cells are continuously released from the PR-PRP matrix, whereas α2 antiplasmin acts by blocking plasmin activity, reducing the proteolytic fibrinolytic breakdown.</p>
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<p>Illustration of the biological features of a PR-PRP matrix. The beneficial effects of an accurately prepared and applied PR-PRP matrix in pathological microenvironments are depicted by several biologically induced processes that are crucial in the repair and regeneration of diseased tissues. The PR-PRP matrix, which is composed of concentrated and activated fibrinogen as its main component, serves as a temporary dense insoluble three-dimensional scaffold with high concentrations of PRP cellular content embedded. Importantly, the matrix enhances the viability and functionality of the PRP cellular content. The PR-PRP matrix is instrumental in providing a molecular link for invading local tissue-resident cells, such as MSCs, macrophages, fibroblasts, and ECs. Inside the matrix microenvironment, a multitude of cells and molecules engage in many cellular interactions. Upon fibrinolytic breakdown of the PR-PRP matrix, an abundance of activated platelets, their PGFs, and other biologically active molecules and cells are released to the local microenvironment. Ultimately, the sustained release of matrix substances leads to an increase in cellular activity and signaling, angiogenetic and immunomodulatory processes, and antimicrobial activities, contributing to the overall tissue repair and regenerative process. Moreover, as a result of the breaking down of fibrin strands, they provide structural support for the development of new tissues and facilitate the adhesion and migration of cells [<a href="#B40-ijms-25-07914" class="html-bibr">40</a>,<a href="#B185-ijms-25-07914" class="html-bibr">185</a>,<a href="#B191-ijms-25-07914" class="html-bibr">191</a>,<a href="#B192-ijms-25-07914" class="html-bibr">192</a>,<a href="#B193-ijms-25-07914" class="html-bibr">193</a>,<a href="#B194-ijms-25-07914" class="html-bibr">194</a>,<a href="#B195-ijms-25-07914" class="html-bibr">195</a>].</p>
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12 pages, 5384 KiB  
Communication
Plasma Engineering of Co4N/CoN Heterostructure for Boosting Supercapacitor Performance
by Hong Li, Yunzhe Ma, Xulei Zhang, Xiuling Zhang and Lanbo Di
Materials 2024, 17(14), 3529; https://doi.org/10.3390/ma17143529 - 16 Jul 2024
Viewed by 675
Abstract
Supercapacitor electrode materials play a decisive role in charge storage and significantly affect the cost and capacitive performance of the final device. Engineering of the heterostructure of metal–organic framework (MOF)-derived transition metal nitrides (TMNs) can be conducive to excellent electrochemical performance owing to [...] Read more.
Supercapacitor electrode materials play a decisive role in charge storage and significantly affect the cost and capacitive performance of the final device. Engineering of the heterostructure of metal–organic framework (MOF)-derived transition metal nitrides (TMNs) can be conducive to excellent electrochemical performance owing to the synergistic effect, optimized charge transport/mass transfer properties, and high electrical conductivity. In this study, a Co4N/CoN heterostructure was incorporated into a nitrogen-doped support by radio-frequency (RF) plasma after simple pyrolysis of Co-based formate frameworks (Co-MFFs), with the framework structure well retained. Plasma engineering can effectively increase the ratio of Co4N in the Co4N/CoN heterostructure, accelerating the electron transfer rate and resulting in a rough surface due to the reduction effect of high-energy electrons and the etching effect of ions. Benefiting from the plasma modification, the obtained electrode material Co4N/CoN@C-P exhibits a high specific capacitance of 346.2 F·g−1 at a current density of 1 A·g−1, approximately 1.7 times that of CoN/Co4N@C prepared by pyrolysis. The specific capacitance of Co4N/CoN@C-P reaches 335.6 F·g−1 at 10 A·g−1, approximately 96.9% of that at 1 A·g−1, indicating remarkable rate capability. Additionally, the capacitance retention remains at 100% even after 1000 cycles, suggesting excellent cycling stability. The rational design and plasma engineering of the TMN heterostructures at the nanoscale are responsible for the excellent electrochemical performance of this novel composite material. Full article
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<p>Electrochemical performance of Co-MFF, CoN/Co<sub>4</sub>N@C, and Co<sub>4</sub>N/CoN@C-P electrodes in 6 M KOH electrolyte with a three-electrode system. (<b>a</b>) CV curves at 10 mV·s<sup>−1</sup>; (<b>b</b>) GCD curves at 1 A·g<sup>−1</sup>; (<b>c</b>) EIS curves; (<b>d</b>) CV profiles of Co<sub>4</sub>N/CoN@C-P at different scan rates; (<b>e</b>) GCD curves of Co<sub>4</sub>N/CoN@C-P at different current densities; (<b>f</b>) Capacitance retention and coulombic efficiency of the Co<sub>4</sub>N/CoN@C-P over 1000 cycles at 1 A·g<sup>−1</sup>.</p>
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<p>XRD patterns of Co-MFF, CoN/Co<sub>4</sub>N@C, and Co<sub>4</sub>N/CoN@C-P.</p>
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<p>Typical SEM images of (<b>a</b>–<b>c</b>) Co-MFF, (<b>d</b>–<b>f</b>) CoN/Co<sub>4</sub>N@C, and (<b>g</b>–<b>i</b>) Co<sub>4</sub>N/CoN@C-P.</p>
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<p>HRTEM images and EDS elemental mappings of the Co, N, and C elements for (<b>a</b>,<b>b</b>) CoN/Co<sub>4</sub>N@C and (<b>c</b>,<b>d</b>) Co<sub>4</sub>N/CoN@C-P (The red dash lines indicate the heterointerface).</p>
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<p>XPS spectra of (<b>a</b>) C1s, (<b>b</b>) Co2p, and (<b>c</b>) N1s for CoN/Co<sub>4</sub>N@C and Co<sub>4</sub>N/CoN@C-P.</p>
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13 pages, 719 KiB  
Article
Assessment of the Concentrations of Selected Aminothiols in Patients after COVID-19
by Izabela Szołtysek-Bołdys, Wioleta Zielińska-Danch, Danuta Łoboda, Krzysztof S. Gołba and Beata Sarecka-Hujar
J. Clin. Med. 2024, 13(14), 4108; https://doi.org/10.3390/jcm13144108 - 14 Jul 2024
Cited by 1 | Viewed by 1014
Abstract
Background: Data show that due to endothelial damage and thrombogenic effects, severe acute respiratory syndrome coronavirus-2 (SARS-CoV-2) infection may accelerate the development of atherosclerosis and increase the risk of cardiovascular diseases (CVDs). The impaired metabolism of aminothiols increases oxidative stress, as these [...] Read more.
Background: Data show that due to endothelial damage and thrombogenic effects, severe acute respiratory syndrome coronavirus-2 (SARS-CoV-2) infection may accelerate the development of atherosclerosis and increase the risk of cardiovascular diseases (CVDs). The impaired metabolism of aminothiols increases oxidative stress, as these molecules are involved in antioxidant defense as well as in thiol redox control. In this study, total levels of selected aminothiols (i.e., cysteine (Cys), homocysteine (HCy), and glutathione) in convalescents after coronavirus disease of 2019 (COVID-19) were evaluated. The analyses were made according to the sex of the patients, time from COVID-19 onset, and COVID-19 severity. Methods: The study group consisted of 212 patients after COVID-19. Levels of total aminothiols were assessed in the blood plasma using high-performance liquid chromatography (HPLC). Results: The mean Cys concentrations were higher in men than in women (229.92 µmol/L ± 51.54 vs. 210.35 µmol/L ± 41.90, respectively; p = 0.003). Differences in Cys levels were also noticed in the total study group between patients distinguished due to time from disease onset (226.82 µmol/L ± 40.57 in <12 weeks, 232.23 µmol/L ± 47.99 in patients 12–24 weeks, and 208.08 µmol/L ± 48.43 in patients >24 weeks; p = 0.005). In addition, over 11% of total patients 12–24 weeks from disease onset had Cys levels above 300 µmol/L compared to almost 4% of patients <12 weeks and 2% of patients >24 weeks (p = 0.046). In sex-adjusted subgroups, significant differences due to time from COVID-19 were found in Cys levels in women (p = 0.004) and in glutathione levels in men (p = 0.024). None of the aminothiol levels differed between the subgroups based on the severity of COVID-19. Conclusions: Men had overall higher Cys levels than women. Cys levels were lower >24 weeks after COVID-19 onset than in the earlier period after disease onset. A partial elevation in Cys levels 12–24 weeks after the disease onset may contribute to the increase in CVD risk in the post-COVID-19 period. Full article
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<p>The frequencies of hyperhomocysteinemia and hypercysteinemia in sex subgroups of patients with COVID-19.</p>
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<p>Mean (M) Cys and glutathione levels depending on time from the COVID-19 onset in sex subgroups. (<b>A</b>)—female subgroup; * post hoc analysis: &lt;12 vs. &gt;24, <span class="html-italic">p</span> = 0.018 and 12–24 vs. &gt;24, <span class="html-italic">p</span> = 0.031; (<b>B</b>)—male subgroup; ** post hoc analysis: 12–24 vs. &gt;24, <span class="html-italic">p</span> = 0.021. The standard deviation (SD) bars are presented in the chart. Significant differences are in bold.</p>
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26 pages, 954 KiB  
Systematic Review
The Incorporation of Zinc into Hydroxyapatite and Its Influence on the Cellular Response to Biomaterials: A Systematic Review
by Jessica Dornelas, Giselle Dornelas, Alexandre Rossi, Adriano Piattelli, Natalia Di Pietro, Tea Romasco, Carlos Fernando Mourão and Gutemberg Gomes Alves
J. Funct. Biomater. 2024, 15(7), 178; https://doi.org/10.3390/jfb15070178 - 28 Jun 2024
Cited by 4 | Viewed by 990
Abstract
Zinc is known for its role in enhancing bone metabolism, cell proliferation, and tissue regeneration. Several studies proposed the incorporation of zinc into hydroxyapatite (HA) to produce biomaterials (ZnHA) that stimulate and accelerate bone healing. This systematic review aimed to understand the physicochemical [...] Read more.
Zinc is known for its role in enhancing bone metabolism, cell proliferation, and tissue regeneration. Several studies proposed the incorporation of zinc into hydroxyapatite (HA) to produce biomaterials (ZnHA) that stimulate and accelerate bone healing. This systematic review aimed to understand the physicochemical characteristics of zinc-doped HA-based biomaterials and the evidence of their biological effects on osteoblastic cells. A comprehensive literature search was conducted from 2022 to 2024, covering all years of publications, in three databases (Web of Science, PUBMED, Scopus), retrieving 609 entries, with 36 articles included in the analysis according to the selection criteria. The selected studies provided data on the material’s physicochemical properties, the methods of zinc incorporation, and the biological effects of ZnHA on bone cells. The production of ZnHA typically involves the wet chemical synthesis of HA and ZnHA precursors, followed by deposition on substrates using processes such as liquid precursor plasma spraying (LPPS). Characterization techniques confirmed the successful incorporation of zinc into the HA lattice. The findings indicated that zinc incorporation into HA at low concentrations is non-cytotoxic and beneficial for bone cells. ZnHA was found to stimulate cell proliferation, adhesion, and the production of osteogenic factors, thereby promoting in vitro mineralization. However, the optimal zinc concentration for the desired effects varied across studies, making it challenging to establish a standardized concentration. ZnHA materials are biocompatible and enhance osteoblast proliferation and differentiation. However, the mechanisms of zinc release and the ideal concentrations for optimal tissue regeneration require further investigation. Standardizing these parameters is essential for the effective clinical application of ZnHA. Full article
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<p>PRISMA flowchart for the systematic review detailing the database searches, the number of abstracts screened, and the full texts selected for the analysis.</p>
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<p>A representative image shows the effects of zinc-doped hydroxyapatite (ZnHA) on osteoblasts and its role in bone regeneration. ZnHA can release Zn<sup>2+</sup>, which directly affects mesenchymal stem cells and osteoblasts, enhancing the expression of RUNX-2, a key transcription factor of osteogenesis. This up-regulation leads to increased levels of bone formation markers such as ALP (Alkaline Phosphatase), Col-1 (Collagen type I), OCN (Osteocalcin), and OP (Osteopontin). The resulting improved osteoblastic activity promotes bone regeneration. However, ZnHA containing zinc above 8% presented cytotoxicity to bone cells.</p>
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12 pages, 13784 KiB  
Article
Enhanced Photoluminescence of Plasma-Treated Recycled Glass Particles
by Zdeněk Remeš, Oleg Babčenko, Vítězslav Jarý and Klára Beranová
Nanomaterials 2024, 14(13), 1091; https://doi.org/10.3390/nano14131091 - 25 Jun 2024
Viewed by 1130
Abstract
Recycled soda-lime glass powder is a sustainable material that is also often considered a filler in cement-based composites. The changes in the surface properties of the glass particles due to the treatments were analyzed by X-ray photoelectron spectroscopy (XPS) and optical spectroscopy. We [...] Read more.
Recycled soda-lime glass powder is a sustainable material that is also often considered a filler in cement-based composites. The changes in the surface properties of the glass particles due to the treatments were analyzed by X-ray photoelectron spectroscopy (XPS) and optical spectroscopy. We have found that there is a relatively high level of carbon contamination on the surface of the glass particles (around 30 at.%), so plasma technology and thermal annealing were tested for surface cleaning. Room temperature plasma treatment was not sufficient to remove the carbon contamination from the surface of the recycled glass particles. Instead, the room temperature plasma treatment of recycled soda-lime glass particles leads to a significant enhancement in their room temperature photoluminescence (PL) by increasing the intensity and accelerating the decay of the photoluminescence. The enhanced blue PL after room-temperature plasma treatment was attributed to the presence of carbon contamination on the glass surface and associated charge surface and interfacial defects and interfacial states. Therefore, we propose blue photoluminescence under UV LED as a fast and inexpensive method to indicate carbon contamination on the surface of glass particles. Full article
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<p>SEM image of the as-received micro-milled waste glass powder.</p>
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<p>The normalized FTIR absorbance spectra measured in an FTIR spectrometer with an ATR accessory after low-pressure plasma treatment at room temperature (<b>a</b>) and at 500 °C (<b>b</b>).</p>
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<p>IR Raman spectra measured with an FTIR spectrometer with 1064 nm laser excitation after low-pressure plasma treatment at room temperature (<b>a</b>) and at 500 °C (<b>b</b>).</p>
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<p>C 1s (<b>a</b>), and O 1s (<b>b</b>) XPS spectra (from top to bottom) for the “as-received” sample, with the samples treated in H<sub>2</sub>, N<sub>2</sub>, and O<sub>2</sub> plasma at room temperature; annealed in H<sub>2</sub>, N<sub>2</sub>, and O<sub>2</sub> atmosphere at 500 °C; and annealed in H<sub>2</sub>, N<sub>2</sub>, and O<sub>2</sub> plasma at 500 °C. Dots represent the measured data, black lines are the results of fits, and colored lines are the fitting components. The peaks shaded by grey originate from carbon–oxygen contamination.</p>
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<p>Ratio of selected components derived from fitting XPS spectra. We use the following labels for simplification: BO: Si-O-Si bridging oxygen, NBO: Si-O-M non-bridging oxygen, H<sub>2</sub>O: oxygen from hydrous species bound to silicon (H<sub>2</sub>O, Si-OH), CO: carbon–oxygen contaminations (C-O(H), C=O, COOH), C: atomic concentration of carbon normalized to 1.</p>
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<p>PL spectra of treated glass powder oxygen plasma. “RT plasma”, resp. “500 °C plasma” represents the PL spectra measured after room temperature, resp. 500 °C O<sub>2</sub> plasma treatment, the PL spectra of as-received and annealed-at-500 °C-in-O<sub>2</sub>-atmosphere (no plasma) glass powder were added for comparison.</p>
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<p>PL spectra (red curve, left axis) of room-temperature H<sub>2</sub> plasma-treated glass powder using sinusoidal UV LED excitation at a frequency of 100 kHz and the spectrally resolved mean time of PL decay (black points with error bars, right axis) evaluated from the phase shift between the excitation and emission (<b>a</b>). The curve with error bars corresponds to the spectrally resolved mean PL decay time τ calculated from the phase shift between the excitation and the emission spectra. The time-resolved PL emission measured by TCSPC at 450 nm is shown in (<b>b</b>). The instrumental response shape measured at the excitation pulse wavelength (blue curve) and fitted function (red curve) were added in (<b>b</b>) for comparison. All measurements were performed at RT.</p>
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20 pages, 7763 KiB  
Article
Comparative Experimental Study on the De-Icing Performance of Multiple Actuators
by Jiajun Zhang, Hua Liang, Biao Wei, Dongliang Bian, Shimin Liu and Hongrui Liu
Actuators 2024, 13(6), 226; https://doi.org/10.3390/act13060226 - 17 Jun 2024
Viewed by 648
Abstract
The issue of aircraft icing poses a substantial threat to flight safety. In order to investigate more efficient anti-icing and de-icing technologies, a comparative analysis was conducted on the de-icing characteristics of three types of actuator materials under varying conditions. Initially, experimental research [...] Read more.
The issue of aircraft icing poses a substantial threat to flight safety. In order to investigate more efficient anti-icing and de-icing technologies, a comparative analysis was conducted on the de-icing characteristics of three types of actuator materials under varying conditions. Initially, experimental research was undertaken to analyze the temperature traits of three actuators under ice-free conditions. Three power densities were chosen for the experiment: 0.170 W/cm2, 0.727 W/cm2, and 1.427 W/cm2. The research findings revealed distinct characteristics: plasma actuators and resistance wire actuators exhibited a strip-like high-temperature region during operation, with well-defined boundaries between the high-temperature and low-temperature zones, whereas ceramic-based semiconductor actuators showcased a uniform high-temperature region. As energy consumption rose, the thermal equilibrium temperatures of all three types tended to converge, with resistance wire actuators operating at 1.427 W/cm2, showing the highest temperature rise rate at that power density. Subsequently, experimental research was carried out on the de-icing performance of three actuators under icing conditions at a specific power density. Following 120 s of de-icing, the ice layer covering the surface of the plasma actuator completely melted, forming a cavity. Conversely, the ice layer on the ceramic-based semiconductor actuator remained partially intact in a strip shape. Ice deposits were still visible on the surface of the resistance wire actuator. This observation highlights the remarkable de-icing speed of the plasma actuator. The propulsive force of plasma generated on the fluid inside the ice layer enhances heat transfer efficiency, thereby accelerating the de-icing process of the plasma actuator at the same power density. The analysis of the de-icing performance of these three novel types of actuators establishes a robust groundwork for exploring more effective aircraft de-icing methods. Furthermore, it furnishes theoretical underpinning for the advancement of composite anti-icing and de-icing strategies. Full article
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<p>Measurement system.</p>
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<p>Physical picture of the actuator: (<b>a</b>) physical image of plasma actuator; (<b>b</b>) physical diagram of ceramic-based semiconductor actuator; (<b>c</b>) physical diagram of resistance wire actuator.</p>
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<p>Output voltage waveform of nanosecond pulse power supply.</p>
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<p>Physical picture of ice layer obtained by freezing method: (<b>a</b>) plasma actuator; (<b>b</b>) ceramic-based semiconductor actuator; The red dashed box in the figure represents the actual size and position of the actuator. (<b>c</b>) resistance wire actuator.</p>
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<p>The ice-making system with water-spray freezing.</p>
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<p>Physical picture of water-cooled semiconductor refrigeration platform.</p>
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<p>Physical picture of plasma actuator using water spray for ice-making.</p>
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<p>Infrared thermal images of the plasma actuator at all times under ice-free conditions: (<b>a</b>) 0.170 W/cm<sup>2</sup>; (<b>b</b>) 0.727 W/cm<sup>2</sup>; (<b>c</b>) 1.427 W/cm<sup>2</sup>.</p>
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<p>The fastest temperature rise curve of the plasma actuator under different power density conditions without ice. The selected power densities are 0.170 W/cm<sup>2</sup>, 0.727 W/cm<sup>2</sup>, and 1.427 W/cm<sup>2</sup>, respectively.</p>
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<p>Dynamic diagram of the de-icing process of plasma actuator under ice conditions at various times.</p>
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<p>Dynamic diagram of the de-icing process of plasma actuator under water-spraying conditions at various times.</p>
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<p>Infrared thermal images of ceramic-based semiconductor actuator at various times under ice-free conditions: (<b>a</b>) 0.170 W/cm<sup>2</sup>; (<b>b</b>) 0.727 W/cm<sup>2</sup>; (<b>c</b>) 1.427 W/cm<sup>2</sup>.</p>
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<p>Temperature rise curves of various power densities for ceramic-based semiconductor actuator under ice-free conditions.</p>
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<p>Dynamic diagram of the de-icing process of the ceramic-based semiconductor actuator under freezing conditions at different times. (The red dashed circle in the picture is used to facilitate readers to see the area of de-icing).</p>
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<p>Infrared thermal images of resistance wire actuators under ice-free conditions at all times: (<b>a</b>) 0.170 W/cm<sup>2</sup>; (<b>b</b>) 0.727 W/cm<sup>2</sup>; (<b>c</b>) 1.427 W/cm<sup>2</sup>.</p>
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<p>Temperature rise curve of resistance wire actuator under different power densities under ice-free conditions.</p>
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<p>De-icing process of resistance wire actuator at different moments under frozen ice conditions.</p>
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<p>Infrared thermal images of different actuators at different times at 0.170 w/cm<sup>2</sup>: (<b>a</b>) plasma actuator; (<b>b</b>) ceramic-based semiconductor actuator; (<b>c</b>) resistance wire actuator.</p>
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<p>Infrared thermal images of different actuators at different times at 0.727 W/cm<sup>2</sup>: (<b>a</b>) plasma actuator; (<b>b</b>) ceramic-based semiconductor actuator; (<b>c</b>) resistance wire actuator.</p>
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<p>Infrared thermal images of different actuators at different times at 1.427 W/cm<sup>2</sup>: (<b>a</b>) plasma actuator; (<b>b</b>) ceramic-based semiconductor actuator; (<b>c</b>) resistance wire actuator.</p>
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<p>The highest temperature rise curve of each actuator under different powers: (<b>a</b>) 0.170 W/cm<sup>2</sup>; (<b>b</b>) 0.727 W/cm<sup>2</sup>; (<b>c</b>) 1.427 W/cm<sup>2</sup>.</p>
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<p>The fastest temperature rise rate of each actuator under different power densities.</p>
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<p>De-icing process diagram of each actuator at different times with a power density of 0.727 w/cm<sup>2</sup>: (<b>a</b>) plasma actuator; (<b>b</b>) ceramic-based semiconductor actuator; (<b>c</b>) resistance wire actuator.</p>
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<p>Flow field analysis of plasma actuator.</p>
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<p>Heat transfer mechanism diagram of plasma actuator de-icing.</p>
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<p>Heat transfer mechanism diagram of different actuators: (<b>a</b>) resistance wire actuator; (<b>b</b>) ceramic-based semiconductor actuator.</p>
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14 pages, 7369 KiB  
Article
Surface Modification of Zr48Cu36Al8Ag8 Bulk Metallic Glass through Glow Discharge Plasma Nitriding
by Krzysztof Kulikowski, Piotr Błyskun, Tomasz Borowski and Tadeusz Kulik
Materials 2024, 17(12), 2850; https://doi.org/10.3390/ma17122850 - 11 Jun 2024
Viewed by 481
Abstract
Bulk metallic glasses are modern engineering materials with unique functional properties. Zr-based alloys are particularly attractive as they exhibit high glass forming ability as well as good mechanical properties. Due to their relatively high thermal stability, reaching as much as 400 °C, they [...] Read more.
Bulk metallic glasses are modern engineering materials with unique functional properties. Zr-based alloys are particularly attractive as they exhibit high glass forming ability as well as good mechanical properties. Due to their relatively high thermal stability, reaching as much as 400 °C, they can be surface-treated in low-temperature plasma to further improve their mechanical properties. The subject of this study was to determine the influence of the technological parameters of nitriding in low-temperature plasma on the structure and mechanical properties of Zr48Cu36Al8Ag8 bulk metallic glass. In the course of this study, the influence of the ion accelerating voltage on the structure and micromechanical properties of the bulk metallic glass was analyzed. The produced samples were characterized in terms of nanohardness, layer adhesion by using the scratch test, and wear resistance by using the ball-on-disc method. As a result of low-temperature plasma nitriding, a significant increase in the surface nanohardness of the Zr48Cu36Al8Ag8 bulk metallic glass was obtained. The produced layers exhibited high adhesion to the substrate and they improved the wear resistance of the glass. The present study indicates the possibility of modifying the surface properties of bulk metallic glasses by using diffusion processes in low-temperature plasma without substrate crystallization. Full article
(This article belongs to the Special Issue Structure and Properties of Metallic Glasses)
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<p>A diagram of the glow discharge nitriding device and an overview of the process.</p>
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<p>A schematic illustration of the “ball-on-disc” method. 1—sample (nitrided BMG); 2—countersample (Al<sub>2</sub>O<sub>3</sub> ball).</p>
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<p>XRD phase analysis of the Zr<sub>48</sub>Cu<sub>36</sub>Al<sub>8</sub>Ag<sub>8</sub> samples after the glow discharge nitriding process at an ion accelerating voltage ranging from 400 to 1000 V at 300 °C for 30 min.</p>
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<p>A SEM cross-section view of the nitride layer prepared on the Zr<sub>48</sub>Cu<sub>36</sub>Al<sub>8</sub>Ag<sub>8</sub> glass at an ion accelerating voltage of 1000 V at 300 °C for 30 min.</p>
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<p>The ion accelerating voltage influence on the nanohardness of the nitrided samples, measured under a 2 mN constant load.</p>
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<p>Nanohardness vs penetration depth for nitride layers prepared using ion accelerating voltage from 400 to 1000 V at 300 °C for 30 min, measured under 39–500 mN load.</p>
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<p>The results of the scratch test obtained for the sample nitrided at an ion accelerating voltage of 400 V: (<b>a</b>) the course of changes in acoustic emission vs load; (<b>b</b>) the friction and penetration depth vs indenter displacement; (<b>c</b>) scratch images in two different areas (I and II).</p>
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<p>The results of the scratch test obtained for the sample nitrided with an ion accelerating voltage of 1000 V: (<b>a</b>) the course of changes in acoustic emission vs load; (<b>b</b>) the friction and penetration depth vs indenter displacement; (<b>c</b>) scratch images in two different areas (I and II).</p>
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<p>Average friction coefficient measured during ball-on-disc wear resistance test of samples nitrided at various ion accelerating voltages.</p>
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<p>The course of changes in the friction coefficient during the ball-on-disc wear resistance test of the samples nitrided at various ion accelerating voltages.</p>
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<p>Surface topography of the wear traces from the ball-on-disc method performed on the initial state sample (IS) as well as on the samples nitrided at various ion accelerating voltages.</p>
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17 pages, 5325 KiB  
Article
The Potential of Sugarcane Waste-Derived Cellulose Fibres as Haemostatic Agents
by Siobhan Malone, Ramanathan Yegappan, Amanda W. Kijas, Anna Gemmell, Alan E. Rowan, Divya Rajah, Minjun Kim, Jan Lauko and Nasim Amiralian
Polymers 2024, 16(12), 1654; https://doi.org/10.3390/polym16121654 - 11 Jun 2024
Viewed by 607
Abstract
Haemorrhage control during surgery and following traumatic injury remains a critical, life-saving challenge. Cellulose products are already employed in commercially available haemostatic dressings. This work explores sourcing cellulose from sugarcane trash pulp to produce micro- and nanosized fibres with hydroxyl, carboxylic acid, and [...] Read more.
Haemorrhage control during surgery and following traumatic injury remains a critical, life-saving challenge. Cellulose products are already employed in commercially available haemostatic dressings. This work explores sourcing cellulose from sugarcane trash pulp to produce micro- and nanosized fibres with hydroxyl, carboxylic acid, and trimethylamine functional groups, resulting in either positive or negative surface charges. This paper assesses the influence of these fibres on multiple blood clotting parameters in both dispersed solutions and dry gauze applications. In vitro blood clotting studies demonstrated the significant haemostatic potential of cellulose fibres derived from sugarcane waste to initiate clotting. Plasma absorbance assays showed that the 0.25 mg/mL cellulose microfibre dispersion had the highest clotting performance. It was observed that no single property of surface charge, functionality, or fibre morphology exclusively controlled the clotting initiation measured. Instead, a combination of these factors affected clot formation, with negatively charged cellulose microfibres comprising hydroxyl surface groups providing the most promising result, accelerating the coagulation cascade mechanism by 67% compared to the endogenous activity. This difference in clot initiation shows the potential for the non-wood agricultural waste source of cellulose in haemostatic wound healing applications, contributing to the broader understanding of cellulose-based materials’ versatility and their applications in biomedicine. Full article
(This article belongs to the Special Issue Advanced Hydrogels for Biomedical Application)
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<p>A schematic overview of the coagulation cascade. The coagulation process can be triggered through either intrinsic (red box) or extrinsic pathways (purple box). Contact with applied haemostatic agents activates the intrinsic pathway. Both pathways lead to the activation of a series of coagulation factors ultimately leading to the activation of factor X, which serves as the common pathway (green box). Upon activation, factor X triggers the conversion of prothrombin into thrombin, initiating the conversion of fibrinogen into fibrin and forming a blood clot.</p>
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<p>Sample preparation flowchart for the transformation of sugarcane trash into various cellulose micro- and nanofibers through chemical treatment and homogenisation.</p>
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<p>Evaluations confirming chemical modifications of the various cellulose forms: (<b>a</b>) FTIR spectra of modified cellulose nanofibres, (<b>b</b>) XRD patterns of all cellulose samples, and (<b>c</b>) BET N<sub>2</sub> adsorption/desorption isotherms for all cellulose samples.</p>
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<p>SEM images of the surface of the (<b>a</b>) CMF, (<b>b</b>) TCMF, (<b>c</b>) CCMF, (<b>d</b>) CNF, (<b>e</b>) TCNF, and (<b>f</b>) CCNF. Scale bars are 10 μm.</p>
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<p>TEM images of the (<b>a</b>) CNF, (<b>b</b>) TCNF, and (<b>c</b>) CCNF. Scale bars are 1 μm.</p>
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<p>Absorption ratio of each cellulose fibre as compared with QuikClot<sup>®</sup> (Qc) Combat Gauze in (<b>a</b>) PBS and (<b>b</b>) whole blood.</p>
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<p>Plasma clotting assay of the control (endogenous activity) as compared with the presence of (<b>a</b>) cellulose microfibre samples of unmodified CMF, TCMF, and CCMF, all at 0.25 mg/mL with (Ca<sup>+</sup>) and without calcium (Ca<sup>−</sup>), and (<b>b</b>) cellulose nanofibre samples of unmodified CNF, TCNF, and CCNF, all at 0.25 mg/mL with (Ca<sup>+</sup>) and without calcium (Ca<sup>−</sup>).</p>
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<p>(<b>a</b>) Average final clotting time (minutes) of whole blood, performed in duplicate. Each assay contained 2 mL of whole blood, 12.5 mM CaCl<sub>2</sub>, and 10 mg of cellulose/gauze material. (<b>b</b>) Photograph taken 20 min after stable clot formation.</p>
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26 pages, 7986 KiB  
Article
Experimental Parametric Study on Flow Separation Control Mechanisms around NACA0015 Airfoil Using a Plasma Actuator with Burst Actuation over Reynolds Numbers of 105–106
by Noritsugu Kubo, Sagar Bhandari, Motofumi Tanaka, Taku Nonomura and Hirokazu Kawabata
Appl. Sci. 2024, 14(11), 4652; https://doi.org/10.3390/app14114652 - 28 May 2024
Viewed by 642
Abstract
Dielectric barrier discharge plasma actuators (DBD-PAs) have the potential to improve the performance of fluid machineries such as aircrafts and wind turbines by preventing flow separation. In this study, to identify the multiple flow control mechanisms in high Reynolds number flow, parametric experiments [...] Read more.
Dielectric barrier discharge plasma actuators (DBD-PAs) have the potential to improve the performance of fluid machineries such as aircrafts and wind turbines by preventing flow separation. In this study, to identify the multiple flow control mechanisms in high Reynolds number flow, parametric experiments for an actuation parameter F+ with a wide range of Re values (105–106) for NACA0015 airfoil was conducted. We conducted wind tunnel tests by applying a DBD-PA to the flow field around a wing model at the leading edge. Lift characteristics, turbulent kinetic energy in the flow field, shear layer height, and the separation point of the boundary layer were evaluated based on pressure distributions on the wing surface and velocity of the flow field, with the effect of DBD-PA on the post-stall flow around the wing and the mechanism behind the increase in the lift coefficient CL analyzed based on these evaluation results. The following phenomena contributed to the increase in CL: (1) increase in turbulent kinetic energy; (2) increase in circulation; and (3) acceleration of the flow near the leading edge. Thus, this study effectively investigated the dependence of the increase in lift on F+ and the lift-increasing mechanism for a wide range of Re values. Full article
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<p>DBD-PA electrode before installation on a wing.</p>
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<p>Schematic of the wind tunnel facility (<b>left</b>) and actual photograph of the wing model (<b>right</b>).</p>
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<p>Schematic of the airfoil shape and pressure port locations.</p>
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<p>Schematic of the DBD-PA installed on the leading edge of the wing model and power supply system.</p>
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<p>Voltage waveform and parameters for DBD-PA actuation.</p>
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<p><math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>L</mi> </msub> </mrow> </semantics></math> curves without DBD-PA actuation.</p>
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<p><math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>p</mi> </msub> </mrow> </semantics></math> distribution on the wing model surface without DBD-PA actuation on each <span class="html-italic">Re</span> number and AoA.</p>
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<p><math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>L</mi> </msub> </mrow> </semantics></math> curves with <math display="inline"><semantics> <mrow> <msup> <mi>F</mi> <mo>+</mo> </msup> </mrow> </semantics></math> = 0.1, 1, 10, and 100 and without DBD-PA actuation for each <span class="html-italic">Re</span> number (<b>a</b>–<b>d</b>), and <math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>L</mi> </msub> </mrow> </semantics></math> increase with respect to <math display="inline"><semantics> <mrow> <msup> <mi>F</mi> <mo>+</mo> </msup> </mrow> </semantics></math> and the angle of attack with DBD-PA actuation for each <span class="html-italic">Re</span> number (<b>e</b>–<b>h</b>).</p>
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<p>PIV results for a typical flow field around the NACA0015 wing model at an angle of attack of 24° (<b>top</b>), and magnified images of the PIV result near the separation point of the boundary layer (<b>bottom</b>). The conditions in this figure are <math display="inline"><semantics> <mrow> <msup> <mi>F</mi> <mrow> <mo>+</mo> </mrow> </msup> <mo>=</mo> <mn>1</mn> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mi>R</mi> <mi>e</mi> <mo>=</mo> <mn>9.4</mn> <mo>×</mo> <msup> <mrow> <mn>10</mn> </mrow> <mn>5</mn> </msup> </mrow> </semantics></math>.</p>
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<p>Schematic defining the position of the boundary layer separation on the <math display="inline"><semantics> <mi>ξ</mi> </semantics></math> axis.</p>
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<p><math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>L</mi> </msub> </mrow> </semantics></math> increase ratio.</p>
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<p>Maximum TKE increase ratio.</p>
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<p>Ratio of the shear layer height.</p>
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<p>Normalized displacement of the separation point of the boundary layer on the wing model with and without DBD-PA actuation.</p>
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<p>PIV results of vorticity fields and velocity vectors for typical flow fields with DBD-PA actuation.</p>
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<p>Comparison of PIV results that show changes in flow pattern by DBD-PA actuation.</p>
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<p><math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>p</mi> </msub> </mrow> </semantics></math> distribution on the wing model surface with changes in flow pattern by DBD-PA actuation on each <span class="html-italic">Re</span> number.</p>
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10 pages, 2340 KiB  
Article
Design of Machine Learning-Based Algorithms for Virtualized Diagnostic on SPARC_LAB Accelerator
by Giulia Latini, Enrica Chiadroni, Andrea Mostacci, Valentina Martinelli, Beatrice Serenellini, Gilles Jacopo Silvi and Stefano Pioli
Photonics 2024, 11(6), 516; https://doi.org/10.3390/photonics11060516 - 28 May 2024
Viewed by 547
Abstract
Machine learning deals with creating algorithms capable of learning from the provided data. These systems have a wide range of applications and can also be a valuable tool for scientific research, which in recent years has been focused on finding new diagnostic techniques [...] Read more.
Machine learning deals with creating algorithms capable of learning from the provided data. These systems have a wide range of applications and can also be a valuable tool for scientific research, which in recent years has been focused on finding new diagnostic techniques for particle accelerator beams. In this context, SPARC_LAB is a facility located at the Frascati National Laboratories of INFN, where the progress of beam diagnostics is one of the main developments of the entire project. With this in mind, we aim to present the design of two neural networks aimed at predicting the spot size of the electron beam of the plasma-based accelerator at SPARC_LAB, which powers an undulator for the generation of an X-ray free electron laser (XFEL). Data-driven algorithms use two different data preprocessing techniques, namely an autoencoder neural network and PCA. With both approaches, the predicted measurements can be obtained with an acceptable margin of error and most importantly without activating the accelerator, thus saving time, even compared to a simulator that can produce the same result but much more slowly. The goal is to lay the groundwork for creating a digital twin of linac and conducting virtualized diagnostics using an innovative approach. Full article
(This article belongs to the Special Issue Recent Advances in Free Electron Laser Accelerators)
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<p>Schematic layout of SPARC linear accelerator principally focused on first meter. In detail, the structure of SPARC’s first meter (1) is shown up to 1.1017 m from the RF gun. There are the solenoid and dipole elements (GUNSOL, GUNDPL01) and the diagnostic system (the scintillating screen or flag AC1FLG01 and the scientific camera AC1CAM01).</p>
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<p>Emittance measurements using ASTRA and SPARC first measure station. The current scan was performed in the range 110–123 A. The measurements converge except for the divergence beyond the minimun beam waist, which was most likely due to machine misalignments.</p>
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<p>Trend of the loss function of the autoencoder network as a function of epochs. The loss asymptotically decreases while increasing the number of epochs, and the minimum value is close to 0 on the order of <math display="inline"><semantics> <mrow> <mn>1</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>5</mn> </mrow> </msup> </mrow> </semantics></math>.</p>
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<p>Variation of the cumulative variance as a function of the number of principal components in PCA. The optimal number of principal components was fixed to 50.</p>
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<p>Trend of the loss function of the predition neural network trained with autoencoder preprocessed simulations as a function of epochs. The loss asymptotically decreases while increasing the number of epochs and the minimum value is closed to 0 on the order of <math display="inline"><semantics> <mrow> <mn>1</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>5</mn> </mrow> </msup> </mrow> </semantics></math>.</p>
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<p>Trend of the loss function of the predition neural network trained with PCA preprocessed simulations as a function of epochs. The loss asymptotically decreases while increasing the number of epochs, and the minimum value is close to 0 on the order of <math display="inline"><semantics> <mrow> <mn>1</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>5</mn> </mrow> </msup> </mrow> </semantics></math>.</p>
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<p>Comparison of two different beam histogram generated with ASTRA simulator (first column) and predicted with the neural network trained on data encoded by the PCA (middle column) and by autoencoder (last column).</p>
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<p>Graph of the loss in terms on MAE during training in relation to the predictions of the x centroid (<b>top left</b>) and y centroid (<b>bottom left</b>) and the x spot size (<b>top right</b>) and y spot size (<b>bottom right</b>) provided by the neural network trained on the simulations encoded by the autoencoder. The red line represents the resolution of the AC1CAM. The best network performance was obtained using 5000 training data.</p>
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<p>Graph of the loss in terms of MAE during training in relation to the predictions of the x centroid (<b>top left</b>) and y centroid (<b>bottom left</b>) and the x spot size (<b>top right</b>) and y spot size (<b>bottom right</b>) provided by the neural network trained on the simulations encoded by the PCA. The red line represents the resolution of the AC1CAM. The best network performance was obtained using 5000 training data.</p>
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<p>Emittance measurement using solenoid scan performed on ASTRA and using both neural networks.</p>
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<p>Energy measurement performed on ASTRA and using both neural networks.</p>
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13 pages, 4882 KiB  
Article
Engineering Nano-Sized Silicon Anodes with Conductive Networks toward a High Average Coulombic Efficiency of 90.2% via Plasma-Assisted Milling
by Yezhan Zuo, Xingyu Xiong, Zhenzhong Yang, Yihui Sang, Haolin Zhang, Fanbo Meng and Renzong Hu
Nanomaterials 2024, 14(8), 660; https://doi.org/10.3390/nano14080660 - 10 Apr 2024
Viewed by 1395
Abstract
Si-based anode is considered one of the ideal anodes for high energy density lithium-ion batteries due to its high theoretical capacity of 4200 mAh g−1. To accelerate the commercial progress of Si material, the multi-issue of extreme volume expansion and low [...] Read more.
Si-based anode is considered one of the ideal anodes for high energy density lithium-ion batteries due to its high theoretical capacity of 4200 mAh g−1. To accelerate the commercial progress of Si material, the multi-issue of extreme volume expansion and low intrinsic electronic conductivity needs to be settled. Herein, a series of nano-sized Si particles with conductive networks are synthesized via the dielectric barrier discharge plasma (DBDP) assisted milling. The p-milling method can effectively refine the particle sizes of pristine Si without destroying its crystal structure, resulting in large Brunauer–Emmett–Teller (BET) values with more active sites for Li+ ions. Due to their unique structure and flexibility, CNTs can be uniformly distributed among the Si particles and the prepared Si electrodes exhibit better structural stability during the continuous lithiation/de-lithiation process. Moreover, the CNT network accelerates the transport of ions and electrons in the Si particles. As a result, the nano-sized Si anodes with CNTs conductive network can deliver an extremely high average initial Coulombic efficiency (ICE) reach of 90.2% with enhanced cyclic property and rate capability. The C-PMSi-50:1 anode presents 615 mAh g−1 after 100 cycles and 979 mAh g−1 under the current density of 5 A g−1. Moreover, the manufactured Si||LiNi0.8Co0.1Mn0.1O2 pouch cell maintains a high ICE of >85%. This work may supply a new insight for designing the nano-sized Si and further promoting its commercial applications. Full article
(This article belongs to the Topic Advanced Nanomaterials for Lithium-Ion Batteries)
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Graphical abstract

Graphical abstract
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<p>(<b>a</b>) XRD patterns of pristine Si and P-milling samples. SEM and HRSEM images of (<b>b</b>) pristine Si and P-milling particles with a mass ratio of (<b>c</b>) 10:1, (<b>d</b>) 20:1, (<b>e</b>) 50:1, and (<b>f</b>) 100:1.</p>
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<p>Nitrogen adsorption and desorption curves with analysis of the BET results of (<b>a</b>) pristine Si and p-milling samples with a mass ratio of (<b>b</b>) 10:1, (<b>c</b>) 20:1, (<b>d</b>) 50:1, and (<b>e</b>) 100:1. (<b>f</b>) Surface area for the pristine Si and P-milling samples.</p>
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<p>Initial CV curves of (<b>a</b>) C-PMSi-50:1 and (<b>b</b>) PMSi-50:1 anodes under a scan rate of 0.1 mV s-1. Initial galvanostatic charge–discharge curves of (<b>c</b>) C-PMSi and (<b>d</b>) PMSi anodes. Enlarged view of GCD curves of (<b>e</b>) C-PMSi and (<b>f</b>) PMSi anodes. Initial Coulombic efficiency of (<b>g</b>) C-PMSi and (<b>h</b>) PMSi anodes. (<b>i</b>) Comparisons of the ICE with recent literature reports [<a href="#B34-nanomaterials-14-00660" class="html-bibr">34</a>,<a href="#B35-nanomaterials-14-00660" class="html-bibr">35</a>,<a href="#B36-nanomaterials-14-00660" class="html-bibr">36</a>,<a href="#B37-nanomaterials-14-00660" class="html-bibr">37</a>,<a href="#B38-nanomaterials-14-00660" class="html-bibr">38</a>,<a href="#B39-nanomaterials-14-00660" class="html-bibr">39</a>,<a href="#B40-nanomaterials-14-00660" class="html-bibr">40</a>,<a href="#B41-nanomaterials-14-00660" class="html-bibr">41</a>,<a href="#B42-nanomaterials-14-00660" class="html-bibr">42</a>].</p>
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<p>Rate capability of (<b>a</b>) C-PMSi and (<b>b</b>) PMSi anodes with the corresponding charge–discharge curves of (<b>c</b>) C-PMSi and (<b>d</b>) PMSi anodes. (<b>e</b>) Cyclic property and (<b>f</b>) Coulombic efficiency of PMSi, C-PMSi, and pristine anodes under 0.2 A g<sup>−1</sup>.</p>
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<p>SEM images of the (<b>a</b>,<b>c</b>) surface and (<b>b</b>,<b>d</b>) cross-sections of C-PMSi-50:1 and PMSi-50:1 anodes before and after 5 and 10 cycles.</p>
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<p>Nyquist plots of C-PMSi-50:1 and PMSi-50:1 anodes (<b>a</b>) before and (<b>b</b>) 10th discharge. Impedance parameters of C-PMSi-50:1 and PMSi-50:1 anodes (<b>c</b>) before and (<b>d</b>) 10th discharge.</p>
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<p>(<b>a</b>) Structure diagram of a pouch cell. (<b>b</b>) Initial galvanostatic charge–discharge curves and (<b>c</b>) cyclic property of C-PMSi/G-B||Li and C-PMSi/G-P||Li half-cell. (<b>d</b>) Initial galvanostatic charge–discharge curves and (<b>e</b>) cyclic property of the C-PMSi/G-P||NCM811 full pouch cell.</p>
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21 pages, 5204 KiB  
Article
Apatite as a Record of Magmatic–Hydrothermal Evolution and Metallogenic Processes: The Case of the Hongshan Porphyry–Skarn Cu–Mo Deposit, SW China
by Yao-Wen Zhang, Jing-Jing Zhu, Li-Chuan Pan, Ming-Liang Huang, Dian-Zhong Wang and Zhi-Chao Zou
Minerals 2024, 14(4), 373; https://doi.org/10.3390/min14040373 - 2 Apr 2024
Viewed by 1125
Abstract
Apatite, as a common accessory mineral found in magmatic–hydrothermal deposits, effectively yields geochemical insights that facilitate our understanding of the mineralization process. In this research, multiple generations of magmatic and hydrothermal apatite were observed in the Hongshan porphyry–skarn Cu–Mo deposit in the Yidun [...] Read more.
Apatite, as a common accessory mineral found in magmatic–hydrothermal deposits, effectively yields geochemical insights that facilitate our understanding of the mineralization process. In this research, multiple generations of magmatic and hydrothermal apatite were observed in the Hongshan porphyry–skarn Cu–Mo deposit in the Yidun Terrane in SW China. The geochemical compositions of the apatite were studied using in situ laser ablation–inductively coupled plasma mass spectrometry and an electron probe microanalysis to understand the magmatic–hydrothermal processes leading to ore formation. The apatite (Ap1a) occurs as subhedral to euhedral inclusions hosted in the phenocrysts of the granite porphyry. The Ap1b occurs later than Ap1a in a fine-grained matrix that intersects the earlier phenocrysts. Increases in F/Cl, F/OH, and F/S and decreases in ΣREE and (La/Yb)N from Ap1a to Ap1b suggest the exsolution of a volatile-rich phase from the magma. The skarn hosts three types of hydrothermal apatite (Ap2a, Ap2b, and Ap3), marking the prograde, retrograde, and quartz–sulfide stages of mineralization, respectively. The elemental behaviors of hydrothermal apatite, including the changes in Cl, Eu, As, and REE, were utilized to reflect evolutions in salinity, pH, oxygen fugacity, and fluid compositions. The composition of Ap2a, which occurs as inclusions within garnet, indicates the presence of an early acidic magmatic fluid with high salinity and oxygen fugacity at the prograde skarn stage. The composition of Ap2b, formed by the coupled dissolution-reprecipitation of Ap2a, indicates the presence of a retrograde fluid that is characterized by lower salinity, higher pH, and a significant decrease in oxygen fugacity compared to the prograde fluid. The Ap3 coexists with quartz and sulfide minerals. Based on studies of Ap3, the fluids in the quartz–sulfide stage exhibit relatively reducing conditions, thereby accelerating the precipitation of copper and iron sulfides. This research highlights the potential of apatite geochemistry for tracing magmatic–hydrothermal evolution processes and identifying mineral exploration targets. Full article
(This article belongs to the Section Mineral Deposits)
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<p>The study area’s geology: (<b>a</b>) tectonic setting of Yidun Terrane and Hongshan deposit (after Li et al. [<a href="#B50-minerals-14-00373" class="html-bibr">50</a>]); (<b>b</b>) geological map of Hongshan Cu–Mo deposit (after Peng et al. [<a href="#B48-minerals-14-00373" class="html-bibr">48</a>]); (<b>c</b>) geological cross-section of Hongshan deposit, showing the spatial relationship of orebodies, strata, and intrusions (after Peng et al. [<a href="#B48-minerals-14-00373" class="html-bibr">48</a>]).</p>
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<p>Photographs of major mineral assemblages in the Hongshan Cu–Mo deposit: (<b>a</b>) granite porphyry with large phenocrysts of plagioclase, quartz, K-feldspar, and biotite; (<b>b</b>) garnet skarn is replaced by massive chalcopyrite, pyrrhotite, and quartz inclusions from the quartz–sulfide stage; (<b>c</b>) euhedral garnet grains with oscillatory zoned rim (cross-polarized light); (<b>d</b>) diopside and euhedral allanite grains are replaced by sulfide (cross-polarized light); (<b>e</b>) massive K-feldspar inclusions coexist with sulfide (cross-polarized light); (<b>f</b>) diopside is overprinted by K-feldspar and actinolite, which is replaced by sulfide and calcite (cross-polarized light); (<b>g</b>) garnet is overprinted by K-feldspar and chlorite, which is replaced by quartz (reflected light); (<b>h</b>) fluorite coexists with chalcopyrite, calcite, and quartz (reflected light). Mineral abbreviations: Act is actinolite; Aln is allanite; Ap is apatite; Cal is calcite; Ccp is chalcopyrite; Chl is chlorite; Di is diopside; Fl is fluorite; Grt is garnet; Kfs is K-feldspar; Pl is plagioclase; Po is pyrrhotite; Qtz is quartz.</p>
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<p>Paragenetic sequence diagram for alteration assemblages in the Hongshan skarn. The widths of lines indicate relative abundance levels of minerals. Narrow lines show minor minerals. Dotted lines indicate traces or uncertainties at the stage.</p>
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<p>Photomicrographs of various apatites: (<b>a</b>) euhedral apatite (Ap1a) inclusion inside magmatic biotite phenocryst (plane-polarized light); (<b>b</b>) an assemblage of magnetite and apatite (Ap1a) inclusions in plagioclase (reflected light); (<b>c</b>) euhedral apatite (Ap1a) inclusion in titanite phenocryst (cross-polarized light); (<b>d</b>) quartz phenocryst with apatite (Ap1a) inclusion transected by a matrix of titanite, K-feldspar, quartz, and apatite (Ap1b) along fractures (cross-polarized light); (<b>e</b>) apatite (Ap1b) grains in the matrix (plane-polarized light, BSE and CL images); (<b>f</b>) euhedral garnet with apatite inclusion is replaced by K-feldspar (BSE image); (<b>g</b>) euhedral garnet with apatite inclusion is replaced by K-feldspar, with insert showing the apatite’s core (Ap2a) and rim (Ap2b) (BSE and CL images); (<b>h</b>) euhedral apatite (Ap3) coexists with quartz, sulfide, and calcite from quartz–sulfide stage. The residual garnet and diopside can also be seen (BSE image). Mineral abbreviations: Ap is apatite; Bi is biotite; Cal is calcite; Grt is garnet; Kfs is K-feldspar; Mag is magnetite; Pl is plagioclase; Po is pyrrhotite; Qtz is quartz; Ttn is titanite.</p>
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<p>Chondrite-normalized rare earth element (REE) patterns: (<b>a</b>) apatites (Ap1a and Ap1b); (<b>b</b>) Ap2a; (<b>c</b>) Ap2b; (<b>d</b>) Ap3. Chondritic values are from Sun and McDonough [<a href="#B58-minerals-14-00373" class="html-bibr">58</a>].</p>
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<p>Geochemical signatures of apatite: (<b>a</b>) Mg + Fe + Sr + Pb vs. Mn; (<b>b</b>) ƩREE + Y vs. Mn/Fe. Trend lines adapted from Cao et al. [<a href="#B20-minerals-14-00373" class="html-bibr">20</a>] (<b>a</b>) and Bouzari et al. [<a href="#B34-minerals-14-00373" class="html-bibr">34</a>] (<b>b</b>).</p>
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<p>Magmatic apatite geochemical plots: (<b>a</b>) Cl vs. F, including data for ore-related porphyries (Tongchanggou and Xiuwacu) from Pan et al. [<a href="#B61-minerals-14-00373" class="html-bibr">61</a>] (points with values of less than 3.77 were selected) and for non-mineralization rock (Cilincuo) from Liu et al. [<a href="#B60-minerals-14-00373" class="html-bibr">60</a>]; their major compositions are listed in <a href="#app1-minerals-14-00373" class="html-app">Supplementary Table S4</a>; (<b>b</b>) DP1-2 vs. DP1-1 (after Mao et al. [<a href="#B19-minerals-14-00373" class="html-bibr">19</a>]).</p>
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<p>Volatile characteristics in magmatic apatite: (<b>a</b>) F/Cl vs. F; (<b>b</b>) XF/XCl vs. XF/XOH; calculated following the thermodynamic partitioning model from Li and Hermann [<a href="#B57-minerals-14-00373" class="html-bibr">57</a>].</p>
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<p>Hydrothermal apatite halogens and Fe characteristics: (<b>a</b>) Cl vs. F; (<b>b</b>) Fe vs. Cl. Note: apfu is per formula unit.</p>
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<p>Hydrothermal apatite geochemical signatures and relationships of trace elements: (<b>a</b>) Eu<sub>N</sub>/Eu<sub>N</sub>* vs. ƩREE + Y; (<b>b</b>) Ce vs. Y; (<b>c</b>) Ce vs. Nd; (<b>d</b>) chondrite-normalized (Gd/Yb)<sub>N</sub> vs. (La/Sm)<sub>N</sub>; (<b>e</b>) (Gd/Yb)<sub>N</sub> vs. (La/Yb)<sub>N</sub>; (<b>f</b>) arsenic (As) vs. ƩREE + Y. Eu/Eu* = Eu<sub>N</sub> × (Sm<sub>N</sub> × Gd<sub>N</sub>)<sup>−0.5</sup>. Chondritic values are from Sun and McDonough [<a href="#B58-minerals-14-00373" class="html-bibr">58</a>].</p>
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