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Search Results (1,248)

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21 pages, 1095 KiB  
Review
Effects of Calcium-Oxide-Modified Biochar on the Anaerobic Digestion of Vacuum Blackwater
by Ping Fa Chiang, Teng Ling Zhang, Abdulmoseen Segun Giwa, Ndungutse Jean Maurice, Mugabekazi Joie Claire, Nasir Ali, Ehtisham Shafique and Mohammadtaghi Vakili
Molecules 2025, 30(2), 215; https://doi.org/10.3390/molecules30020215 - 7 Jan 2025
Viewed by 628
Abstract
The increasing global population and urbanization have led to significant challenges in waste management, particularly concerning vacuum blackwater (VBW), which is the wastewater generated from vacuum toilets. Traditional treatment methods, such as landfilling and composting, often fall short in terms of efficiency and [...] Read more.
The increasing global population and urbanization have led to significant challenges in waste management, particularly concerning vacuum blackwater (VBW), which is the wastewater generated from vacuum toilets. Traditional treatment methods, such as landfilling and composting, often fall short in terms of efficiency and sustainability. Anaerobic digestion (AD) has emerged as a promising alternative, offering benefits such as biogas production and digestate generation. However, the performance of AD can be influenced by various factors, including the composition of the feedstock, pH levels, and the presence of inhibitors. This review investigates the effects of calcium oxide (CaO)-modified biochar (BC) as an additive in AD of VBW. Modifying BC with CaO enhances its alkalinity, nutrient retention, and adsorption capacity, creating a more favorable environment for microorganisms and promoting biogas production, which serves as a valuable source of heat, fuel and electricity. Additionally, the digestate can be processed through plasma pyrolysis to ensure the complete destruction of pathogens while promoting resource utilization. Plasma pyrolysis operates at extremely high temperatures, effectively sterilizing the digestate and eliminating both pathogens and harmful contaminants. This process not only guarantees the safety of the end products, but also transforms organic materials into valuable outputs such as syngas and slag. The syngas produced is a versatile energy carrier that can be utilized as a source of hydrogen, electricity, and heat, making it a valuable resource for various applications, including fuel cells and power generation. Furthermore, the slag has potential for reuse as an additive in the AD process or as a biofertilizer to enhance soil properties. This study aims to provide insights into the benefits of using modified BC as a co-substrate in AD systems. The findings will contribute to the development of more sustainable and efficient waste management strategies, addressing the challenges associated with VBW treatment while promoting renewable energy production. Full article
(This article belongs to the Topic Advances in Organic Solid Waste and Wastewater Management)
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<p>Simple route of biochar production and modification.</p>
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<p>Schematic representation of calcium-oxide-modified biochar as an additive in anaerobic digestion of vacuum blackwater co-processed with plasma pyrolysis.</p>
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20 pages, 12122 KiB  
Article
Microstructural and Mechanical Characterization of Nb-Doped MoS2 Coatings Deposited on H13 Tool Steel Using Nb-Based Interlayers
by Miguel R. Danelon, Newton K. Fukumasu, Angelo A. Carvalho, Ronnie R. Rego, Izabel F. Machado, Roberto M. Souza and André P. Tschiptschin
Coatings 2025, 15(1), 57; https://doi.org/10.3390/coatings15010057 - 6 Jan 2025
Viewed by 476
Abstract
Molybdenum disulfide is a 2D material with excellent lubricant properties, resulting from weak van der Waals forces between lattice layers and shear-induced crystal orientation. The low forces needed to shear the MoS2 crystal layers grant the tribological system low coefficients of friction [...] Read more.
Molybdenum disulfide is a 2D material with excellent lubricant properties, resulting from weak van der Waals forces between lattice layers and shear-induced crystal orientation. The low forces needed to shear the MoS2 crystal layers grant the tribological system low coefficients of friction (COF). However, film oxidation harms its efficacy in humid atmospheres, leading to an increased COF and poor surface adhesion, making its use preferable in dry or vacuum conditions. To overcome these challenges, doping MoS2 with elements such as Nb, Ti, C, and N emerges as a promising solution. Nevertheless, the adhesion of these coatings to a steel substrate presents challenges and strategies involving the reduction in residual stresses and increased chemical affinity to the substrate by using niobium-based materials as interlayers. In this study, Nb-doped MoS2 films were deposited on H13 steel and silicon wafers using the pulsed direct current balanced magnetron sputtering technique. Different niobium-based interlayers (pure Nb and NbN) were deposited to evaluate the adhesion properties of Nb-doped MoS2 coatings. Unlubricated scratch tests, conducted at room temperature and relative humidity under a progressive load, were performed to analyze the COF and adhesion of the coating. Instrumented indentation tests were conducted to assess the hardness and elastic modulus of the coatings. The microstructure of the coatings was obtained by Scanning Electron Microscopy (SEM), Scanning Transmission Electron Microscopy (STEM), and Transmission Electron Microscopy (TEM), with Energy-Dispersive X-Ray Spectroscopy (EDS). Results indicated that niobium doping on MoS2 coatings changes the structure from crystalline to amorphous. Additionally, the Nb concentration of the Nb:MoS2 coating changed the mechanical properties, leading to different cohesive failures by different loads during the scratch tests. Results have also indicated that an NbN interlayer optimally promoted the adhesion of the film. This result is justified by the increase in hardness led by higher Nb concentrations, enhancing the load-bearing capacity of the coating. It is concluded that niobium-based materials can be used to enhance the adhesion properties of Nb-doped MoS2 films and improve their tribological performance. Full article
(This article belongs to the Special Issue Friction, Wear, Lubrication and Mechanics of Surfaces and Interfaces)
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<p>(<b>A</b>) Scheme of deposition and (<b>B</b>) architecture of Nb:MoS<sub>2</sub> coatings.</p>
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<p>Microstructures of Nb:MoS<sub>2</sub> coatings deposited under different powers applied to the Nb target: (<b>A</b>) 25 W, (<b>B</b>) 30 W, (<b>C</b>) 35 W, and (<b>D</b>) 40 W.</p>
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<p>Microstructure of Nb25NbN300 sample at SEM.</p>
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<p>FEG Nb30NbN300 film microstructure. The Pt light gray layer was deposited on the surface to protect the film from being damaged by the focused ion beam.</p>
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<p>EDS analysis of the cross-section of different layers.</p>
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<p>TEM image of the transition between Pt, MoS<sub>2</sub>, and Nb:MoS<sub>2</sub> layers.</p>
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<p>TEM images of the (<b>A</b>) pure MoS<sub>2</sub> layer, (<b>B</b>) Nb:MoS<sub>2</sub> film, and (<b>C</b>) scheme of the crystal structure of a MoS<sub>2</sub> monolayer showing a layer of molybdenum (blue) sandwiched between two layers of sulfur (yellow).</p>
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<p>TEM images of the (<b>A</b>) MoS<sub>2</sub> and (<b>C</b>) Nb:MoS<sub>2</sub> layers. Red circles indicate regions for SAED analysis, with corresponding patterns in (<b>B</b>) and (<b>D</b>), respectively.</p>
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<p>TEM images of the (<b>A</b>) MoS<sub>2</sub> and (<b>C</b>) Nb:MoS<sub>2</sub> layers. Red circles indicate regions for SAED analysis, with corresponding patterns in (<b>B</b>) and (<b>D</b>), respectively.</p>
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<p>The transition between the NbN and Nb layers shows partial epitaxial growth. The blue line was included as an indication of the interface between both layers.</p>
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<p>TEM images of the (<b>A</b>) NbN and (<b>B</b>) Nb layers. Red circles indicate regions for SAED analysis, with corresponding patterns in (<b>C</b>) and (<b>D</b>), respectively.</p>
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<p>Raman spectroscopy of niobium nitride from NbN300 sample. The insert was taken from [<a href="#B58-coatings-15-00057" class="html-bibr">58</a>].</p>
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<p>Scratch images of samples (<b>A</b>) Nb25, (<b>B</b>) Nb30, (<b>C</b>) Nb35, (<b>D</b>) Nb40, and (<b>E</b>) Nb25NbN300.</p>
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<p>Graphs of COF, tangential force, and normal force as a function of the distance of the scratch for the samples (<b>A</b>) Nb25, (<b>B</b>) Nb30, (<b>C</b>) Nb35, (<b>D</b>) Nb40, and (<b>E</b>) Nb25NbN300.</p>
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<p>Characterization of cohesive failure of coatings by (<b>A</b>) optical microscope and (<b>B</b>) SEM.</p>
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<p>Characterization of adhesive failure by (<b>A</b>) optical microscope, (<b>B</b>) SEM and EDS, and (<b>C</b>) combined analysis of COF curve and scratch image.</p>
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<p>Characterization of adhesive failure by (<b>A</b>) optical microscope, (<b>B</b>) SEM and EDS, and (<b>C</b>) combined analysis of COF curve and scratch image.</p>
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12 pages, 4570 KiB  
Article
Effect of Nitrogen Ratio in Sputtering on the Quality of Film Formation and Electron Emission Properties of Nitride Films
by Yuqing Gu, Juannan Li, Dan Wang and Na Zhang
Coatings 2025, 15(1), 55; https://doi.org/10.3390/coatings15010055 - 6 Jan 2025
Viewed by 368
Abstract
Nitride films such as tantalum nitride (TaN), titanium nitride (TiN) and boron nitride (BN) are widely used in aerospace and vacuum electronics. The electron emitting properties of these nitride films are of great interest due to the phenomenon of surface electron emission when [...] Read more.
Nitride films such as tantalum nitride (TaN), titanium nitride (TiN) and boron nitride (BN) are widely used in aerospace and vacuum electronics. The electron emitting properties of these nitride films are of great interest due to the phenomenon of surface electron emission when the films are irradiated, leading to surface modification. In this study, we have prepared three kinds of thin films, TaN, TiN and BN, by sputtering. Then the effect of the nitrogen component on the film formation quality and the dependence of the electron emission coefficient (EEC) on the film’s physical properties were investigated. The results of elemental analysis show that by rising the nitrogen gas flow during sputtering, the N elemental ratios inside the TaN and TiN films can be increased, and the film resistivity decreases follow, while BN films do not show such a tunable characteristic of the elemental ratios or resistivity. The conductivity test results show that TaN and TiN films exhibit conductive properties like those of semiconductor materials. The proportion of N elements inside the films has a significant effect on the film conductivity, namely, the conductivity of the film shows an upward trend with the increase in the proportion of N elements. The EEC test shows that TaN and TiN films with good conductive properties have relatively low EEC values, which are generally lower than 2.10. For TaN and TiN, the test results show that the EEC decreases with the increase of the conductivity. The EEC peak values are 1.92 and 1.56 for TaN and TiN films when their resistivities are 1.45 × 10−5 Ω·m and 7.26 × 10−6 Ω·m, respectively. The EEC values of BN are larger than TaN and TiN, with an EEC peak value higher than 2.49, and the electron energy to obtain the peak value is about 250 eV. The results are instructive for revealing the electron emission regularity of nitride thin films. Full article
(This article belongs to the Special Issue Advanced Nanostructured Coatings Deposited by Magnetron Sputtering)
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<p>Surface morphologies and cross-sectional images of three Si-based TaN nanofilms acquired by using SEM characterization.</p>
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<p>Surface elemental component analysis of three Si-based TaN films acquired by using XPS characterization.</p>
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<p>Measured EEC data of the sputtered TaN nanofilms with three different N<sub>2</sub> flows applied.</p>
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<p>Surface morphologies and cross-sectional images of three Si-based TiN nanofilms acquired by using SEM characterization.</p>
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<p>Surface elemental component analysis of three Si-based TiN films acquired by using XPS characterization.</p>
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<p>Measured EEC data of the sputtered TiN nanofilms with three different N<sub>2</sub> flows applied.</p>
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<p>Surface morphologies and cross-sectional images of three Si-based BN nanofilms acquired by using SEM characterization.</p>
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<p>Surface elemental component analysis of three Si-based BN films acquired by using XPS characterization.</p>
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<p>Measured EEC data of the sputtered BN nanofilms with three different N<sub>2</sub> flows applied.</p>
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12 pages, 5879 KiB  
Article
Advanced Thermoelectric Performance of SWCNT Films by Mixing Two Types of SWCNTs with Different Structural and Thermoelectric Properties
by Yutaro Okano, Hisatoshi Yamamoto, Koki Hoshino, Shugo Miyake and Masayuki Takashiri
Materials 2025, 18(1), 188; https://doi.org/10.3390/ma18010188 - 4 Jan 2025
Viewed by 422
Abstract
Semiconducting single-walled carbon nanotubes (SWCNTs) are significantly attractive for thermoelectric generators (TEGs), which convert thermal energy into electricity via the Seebeck effect. This is because the characteristics of semiconducting SWCNTs are perfectly suited for TEGs as self-contained power sources for sensors on the [...] Read more.
Semiconducting single-walled carbon nanotubes (SWCNTs) are significantly attractive for thermoelectric generators (TEGs), which convert thermal energy into electricity via the Seebeck effect. This is because the characteristics of semiconducting SWCNTs are perfectly suited for TEGs as self-contained power sources for sensors on the Internet of Things (IoT). However, the thermoelectric performances of the SWCNTs should be further improved by using the power sources. The ideal SWCNTs have a high electrical conductivity and Seebeck coefficient while having a low thermal conductivity, but it is challenging to balance everything. In this study, to improve the thermoelectric performance, we combined two types of SWCNTs: one with a high electrical conductivity (Tuball 01RW03, OCSiAl) and the other with a high Seebeck coefficient and low thermal conductivity (ZEONANO SG101, ZEON). The SWCNT inks were prepared by mixing two types of SWCNTs using ultrasonic dispersion while varying the mixing ratios, and p-type SWCNT films were prepared using vacuum filtration. The highest dimensionless figure-of-merit of 1.1 × 10−3 was exhibited at approximately 300 K when the SWCNT film contained the SWCNT 75% of SWCNT (ZEONANO SG101) and 25% of SWCNT (Tuball 01RW03). This simple process will contribute to the prevalent use of SWCNT-TEG as a power source for IoT sensors. Full article
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<p>Manufacturing process of SWCNT inks and films.</p>
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<p>Nanostructure of SWCNTs determined by FE-TEM. (<b>a</b>) SWCNT-SG and (<b>b</b>) SWCNT-Tu.</p>
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<p>Microstructure and surface morphology of SWCNT films with different mixing ratios at SWCNT-Tu/(SWCNT-Tu + SWCNT-SG) of (<b>a</b>) 0%, (<b>b</b>) 25%, (<b>c</b>) 50%, (<b>d</b>) 75%, and (<b>e</b>) 100%.</p>
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<p>(<b>a</b>) Raman spectra of the SWCNT films with different mixing ratios of SWCNTs and (<b>b</b>) the relationship between the Raman intensity ratio (<span class="html-italic">I<sub>G</sub></span>/<span class="html-italic">I<sub>D</sub></span>) of the SWCNT films and the mixing ratio of SWCNTs.</p>
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<p>Thermal and physical properties of SWCNT films with different mixing ratios of SWCNTs. (<b>a</b>) In-plane thermal diffusivity, (<b>b</b>) mass density, (<b>c</b>) specific heat, and (<b>d</b>) in-plane thermal conductivity.</p>
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<p>In-plane thermoelectric properties of SWCNT films with different mixing ratios of SWCNTs. (<b>a</b>) Electrical conductivity, (<b>b</b>) Seebeck coefficient, (<b>c</b>) power factor, and (<b>d</b>) dimensionless figure-of-merit.</p>
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22 pages, 2231 KiB  
Article
Vacuum Ultraviolet Spectroscopic Analysis of Structural Phases in TiO2 Sol–Gel Thin Films
by Helena Cristina Vasconcelos, Maria Meirelles, Reşit Özmenteş and Abdulkadir Korkut
Coatings 2025, 15(1), 19; https://doi.org/10.3390/coatings15010019 - 28 Dec 2024
Viewed by 364
Abstract
This study investigates the structural and electronic transitions of sol–gel derived titanium dioxide (TiO2) thin films using vacuum ultraviolet (VUV) spectroscopy, to elucidate the impact of annealing-induced phase evolution. As the annealing temperature increased from 400 °C to 800 °C, the [...] Read more.
This study investigates the structural and electronic transitions of sol–gel derived titanium dioxide (TiO2) thin films using vacuum ultraviolet (VUV) spectroscopy, to elucidate the impact of annealing-induced phase evolution. As the annealing temperature increased from 400 °C to 800 °C, the films transitioned from amorphous to anatase, mixed anatase–rutile, and finally rutile phases. VUV spectroscopy revealed distinct absorption features: a high-energy σ → π* transition below 150 nm, associated with bonding to antibonding orbital excitations, and lower-energy absorption bands in the range 175–180 nm and near 280 nm, attributed to π → π* and t2g(π) → t*2g(π*) transitions, respectively. These spectral features highlight the material’s intrinsic electronic states and defect-related transitions. A slight redshift of the absorption band from 176 nm to 177 nm with annealing reflects bandgap narrowing, attributed to increased rutile content, crystallite growth, and defect-induced effects. Broadening and additional absorption features around 280 nm were attributed to oxygen vacancies and reduced titanium oxidation states (Ti3⁺), as corroborated by X-ray photoelectron spectroscopy (XPS). XPS further confirmed the presence of Ti3⁺ species and oxygen vacancies, providing complementary evidence of defect-mediated transitions observed in the VUV spectra. While complementary techniques such as X-ray diffraction (XRD) and Fourier Transform Infrared Spectroscopy (FTIR) confirmed phase transitions and the reduction of hydroxyl groups, respectively, VUV spectroscopy uniquely captured the dynamic interplay between structural defects, phase evolution, and optical properties. This study underscores the utility of VUV spectroscopy as a powerful tool for probing the electronic structure of TiO2 films, offering insights critical for tailoring their functional properties in advanced applications. Full article
(This article belongs to the Collection Advanced Optical Films and Coatings)
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<p>XRD patterns of TiO<sub>2</sub> thin films under different conditions: (<b>a</b>) as-deposited (amorphous structure); (<b>b</b>) annealed at 400 °C (crystalline anatase phase); (<b>c</b>) annealed at 600 °C (mixed anatase and rutile phases); and (<b>d</b>) annealed at 800 °C (rutile-dominant phase with residual anatase), each for 6 h.</p>
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<p>VUV absorption spectra of sol–gel derived TiO<sub>2</sub> thin films as-deposited and annealed at 400 °C, 600 °C, and 800 °C, illustrating the evolution of electronic transitions with phase transformation: (<b>a</b>) high-energy region (125–230 nm) highlighting the σ → π* transition and the absorption band in the range 175–180 nm; and (<b>b</b>) low-energy region (220–330 nm) showing the t<sub>2</sub>g(π) → t<sub>2</sub>g*(π*) transition and the broad defect-related absorption band around 280 nm.</p>
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<p>VUV absorption spectra of sol–gel derived TiO<sub>2</sub> thin films annealed at 400 °C, 600 °C, and 800 °C, from~155 nm to 200 nm, highlighting the shift in the 176–177 nm absorption peak.</p>
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<p>FTIR spectra of sol–gel derived TiO<sub>2</sub> thin films as-deposited and annealed at 400 °C and 800 °C, in the range 4000 to 1500 cm<sup>−1</sup>, highlighting the evolution of hydroxyl (–OH) groups and water adsorption bands.</p>
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<p>High-resolution Ti 2p XPS spectra of TiO<sub>2</sub> films: (<b>a</b>) Annealed TiO<sub>2</sub> at 400 °C: Peaks at 457.4 eV (Ti<sup>3</sup>⁺ 2p<sub>3</sub>/<sub>2</sub>) and 458.1 eV (Ti<sup>4</sup>⁺ 2p<sub>3</sub>/<sub>2</sub>) indicate the presence of both Ti<sup>3</sup>⁺ and Ti<sup>4</sup>⁺ states, reflecting the formation of Ti<sup>3</sup>⁺ defects and oxygen vacancies during the crystallization of TiO<sub>2</sub> into the anatase phase. (<b>b</b>) As-deposited TiO<sub>2</sub>: The spectrum primarily shows the Ti<sup>4</sup>⁺ oxidation state at 458.1 eV (Ti<sup>4</sup>⁺ 2p<sub>3</sub>/<sub>2</sub>) with no significant Ti<sup>3</sup>⁺ peaks, indicating the amorphous nature of the film and the lack of Ti<sup>3</sup>⁺ states.</p>
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<p>High-resolution O 1s XPS spectra of TiO<sub>2</sub> films: (<b>a</b>) As-deposited TiO<sub>2</sub>: peaks at 529.2 eV (lattice oxygen) and 531.7 eV (surface-bound oxygen species, including OH and O<sub>2</sub>). (<b>b</b>) Annealed TiO<sub>2</sub> at 400 °C: main peak at 531.3 eV with a shoulder at 533.2 eV, indicating adsorbed oxygen species and oxygen vacancies.</p>
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18 pages, 8051 KiB  
Article
Comparative Investigation of Vortex and Direct Plasma Discharge for Treating Titanium Surface
by Hyun-Jeong Jeon, Subin Seo, Ara Jung, Kyeong-mok Kang, Jeonghoon Lee, Bomi Gweon and Youbong Lim
Biomimetics 2025, 10(1), 7; https://doi.org/10.3390/biomimetics10010007 - 26 Dec 2024
Viewed by 398
Abstract
Numerous studies have investigated the surface treatment of implants using various types of plasma, including atmospheric pressure plasma and vacuum plasma, to remove impurities and increase surface energy, thereby enhancing osseointegration. Most previous studies have focused on generating plasma directly on the implant [...] Read more.
Numerous studies have investigated the surface treatment of implants using various types of plasma, including atmospheric pressure plasma and vacuum plasma, to remove impurities and increase surface energy, thereby enhancing osseointegration. Most previous studies have focused on generating plasma directly on the implant surface by using the implant as an electrode for plasma discharge. However, plasmas generated under atmospheric and moderate vacuum conditions often have a limited plasma volume, meaning the shape of the electrodes significantly influences the local electric field characteristics, which in turn affects plasma behavior. Consequently, to ensure consistent performance across implants of different sizes and shapes, it is essential to develop a plasma source with discharge characteristics that are unaffected by the treatment target, ensuring uniform exposure. To address this challenge, we developed a novel plasma source, termed “vortex plasma”, which generates uniform plasma using a magnetic field within a controlled space. We then compared the surface treatment efficiency of the vortex plasma to that of conventional direct plasma discharge by evaluating hydrophilicity, surface chemistry, and surface morphology. In addition, to assess the biological outcomes, we examined osteoblast cell activity on both the vortex and direct plasma-treated surfaces. Our results demonstrate that vortex plasma improved hydrophilicity, reduced carbon content, and enhanced osteoblast adhesion and activity to a level comparable to direct plasma, all while maintaining the physical surface structure and morphology. Full article
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Graphical abstract

Graphical abstract
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<p>(<b>a</b>) Piping and instrument diagram of the plasma activator (side view) and (<b>b</b>) device image and key functional elements in the front view.</p>
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<p>Configuration of the container with (<b>a</b>) conceptual and (<b>b</b>) actual drawing.</p>
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<p>Configurations of electric and magnetic field for (<b>a</b>) direct and (<b>b</b>) vortex plasma discharge.</p>
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<p>Discharge configurations and image for (<b>a</b>) direct and (<b>b</b>) vortex plasma.</p>
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<p>(<b>a</b>) Representative images of the contact angle measured for each sample and (<b>b</b>) measurement results of the contact angle. *, <span class="html-italic">p</span> &lt; 0.001; #, <span class="html-italic">p</span> &lt; 0.05 (Unpaired student’s <span class="html-italic">t</span>-test. * mark was compared to the Control, and # mark was compared to D15.).</p>
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<p>Chemical composition of (<b>a</b>) carbon and (<b>b</b>) oxygen on the titanium surface.</p>
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<p>(<b>a</b>) C1s and (<b>b</b>) O1s narrow peaks measured on the surface of each sample.</p>
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<p>Deconvoluted results of the (<b>a</b>,<b>c</b>,<b>e</b>) C1s and (<b>b</b>,<b>d</b>,<b>f</b>) O1s peak. (<b>a</b>,<b>b</b>) Control, (<b>c</b>,<b>d</b>) D15, and (<b>e</b>,<b>f</b>) V30 sample.</p>
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<p>SEM observation of the surface by position on the titanium coupon before and after treatment with direct plasma for 15 s (10,000×).</p>
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<p>SEM observation of the surface by position on the titanium coupon before and after treatment with vortex plasma for 30 s (10,000×).</p>
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<p>ALP Activity on the titanium coupons of the Control, D15, and V30. * <span class="html-italic">p</span> &lt; 0.01, ** <span class="html-italic">p</span> &lt; 0.001 (Unpaired student’s <span class="html-italic">t</span>-test. Data were compared to the Control).</p>
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<p>Representative fluorescence microscopy images of Saos-2 cells adhered to the coupon surfaces for the Control, D15, and V30 groups. The nuclei are shown in grayscale, while actin filaments are shown in red. Scale bar = 100 μm.</p>
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16 pages, 336 KiB  
Article
Vacuum Polarization Energy of a Proca Soliton
by Damian A. Petersen and Herbert Weigel
Symmetry 2025, 17(1), 13; https://doi.org/10.3390/sym17010013 - 25 Dec 2024
Viewed by 268
Abstract
We study an extended Proca model with one scalar field and one massive vector field in one space dimension and one time dimension. We construct the soliton solution and subsequently compute the vacuum polarization energy (VPE), which is the leading quantum correction to [...] Read more.
We study an extended Proca model with one scalar field and one massive vector field in one space dimension and one time dimension. We construct the soliton solution and subsequently compute the vacuum polarization energy (VPE), which is the leading quantum correction to the classical energy of the soliton. For this calculation, we adopt the spectral methods approach, which heavily relies on the analytic properties of the Jost function. This function is extracted from the interaction of the quantum fluctuations with a background potential generated by the soliton. Particularly, we explore eventual non-analytical components that may be induced by mass gaps and the unconventional normalization for the longitudinal component of the vector field fluctuations. By numerical simulation, we verify that these obstacles do not actually arise and that the real and imaginary momentum formulations of the VPE yield equal results. The Born approximation to the The Jost function is crucial when implementing standard renormalization conditions. In this context, we solve problems arising from the Born approximation being imaginary for real momenta associated with energies in the mass gap. Full article
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<p>Total phase shift in the toy model for repulsive (<b>left</b>) and attractive (<b>right</b>) potentials. The parameters for the repulsive case are <math display="inline"><semantics> <mrow> <msub> <mi>m</mi> <mn>1</mn> </msub> <mo>=</mo> <mn>1.5</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mi>m</mi> <mn>2</mn> </msub> <mo>=</mo> <mn>3.5</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>11</mn> </msub> <mo>=</mo> <mn>4.0</mn> <mo>,</mo> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>22</mn> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics></math>, and <math display="inline"><semantics> <mrow> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>12</mn> </msub> <mo>=</mo> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>21</mn> </msub> <mo>=</mo> <mn>2.0</mn> </mrow> </semantics></math>. In that case, the two lines are on top of each other. The attractive potential is parameterized by <math display="inline"><semantics> <mrow> <msub> <mi>m</mi> <mn>1</mn> </msub> <mo>=</mo> <mn>2.0</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mi>m</mi> <mn>2</mn> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>11</mn> </msub> <mo>=</mo> <mo>−</mo> <mn>4.0</mn> <mo>,</mo> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>22</mn> </msub> <mo>=</mo> <mo>−</mo> <mn>3.0</mn> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>12</mn> </msub> <mo>=</mo> <msub> <mover> <mi>v</mi> <mo>¯</mo> </mover> <mn>21</mn> </msub> <mo>=</mo> <mo>−</mo> <mn>0.5</mn> </mrow> </semantics></math>.</p>
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<p>Soliton profiles for <math display="inline"><semantics> <mrow> <mi>g</mi> <mo>=</mo> <mn>1.0</mn> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mi>μ</mi> <mo>=</mo> <mn>1.5</mn> </mrow> </semantics></math> (<b>left panel</b>). The inlay corroborates that <math display="inline"><semantics> <mrow> <msup> <mi>a</mi> <mo>′</mo> </msup> <mrow> <mo>(</mo> <mn>0</mn> <mo>)</mo> </mrow> <mo>=</mo> <mn>0</mn> </mrow> </semantics></math>. Also shown are the fitted profiles for <math display="inline"><semantics> <mi>ϕ</mi> </semantics></math> (<b>middle panel</b>) and <span class="html-italic">a</span> (<b>right panel</b>) in comparison with the solutions to Equation (23), labeled ‘DEQ’.</p>
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17 pages, 11667 KiB  
Article
Silicon Drift Detectors for the Measurement and Reconstruction of Beta Spectra
by Andrea Nava, Leonardo Bernardini, Matteo Biassoni, Tommaso Bradanini, Marco Carminati, Giovanni De Gregorio, Carlo Fiorini, Giulio Gagliardi, Peter Lechner, Riccardo Mancino and Chiara Brofferio
Sensors 2024, 24(24), 8202; https://doi.org/10.3390/s24248202 - 22 Dec 2024
Viewed by 544
Abstract
The ASPECT-BET project, or An sdd-SPECTrometer for BETa decay studies, aims to develop a novel technique for the precise measurement of forbidden beta spectra in the 10 keV–1 MeV range. This technique employs a Silicon Drift Detector (SDD) as the main spectrometer with [...] Read more.
The ASPECT-BET project, or An sdd-SPECTrometer for BETa decay studies, aims to develop a novel technique for the precise measurement of forbidden beta spectra in the 10 keV–1 MeV range. This technique employs a Silicon Drift Detector (SDD) as the main spectrometer with the option of a veto system to reject events exhibiting only partial energy deposition in the SDD. A precise understanding of the spectrometer’s response to electrons is crucial for accurately reconstructing the theoretical shape of the beta spectrum. To compute this response, GEANT4 simulations optimized for low-energy electron interactions are used and validated with a custom-made electron gun. In this article we present the performance of these simulations in reconstructing the electron spectra measured with SDDs of a 109Cd monochromatic source, both in vacuum and in air. The allowed beta spectrum of a 14C source was also measured and analyzed, proving that this system is suitable for the application in ASPECT-BET. Full article
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<p>47-pixel SDD matrix used for all the measurements here reported (<b>left</b>). Scheme of the 47 pixels: only the 7 red ones were acquired (<b>right</b>).</p>
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<p>Vacuum chamber in the Milano-Bicocca laboratory. The main detectors operated in this setup, a 47-pixel SDD matrix and a Pixet, are indicated. The e-gun, attached to a xy-movable stage, is also highlighted.</p>
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<p>(<b>Left</b>): picture of the e-gun. (<b>Center</b>): anode with 7 LEDs used to illuminate the cathode and the aluminum cylinder with UV light. (<b>Right</b>): gold-coated cathode used to collimate the electron beam. The aluminum cylinder, where electrons are produced, is visible in its center.</p>
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<p>(<b>Left</b>): CAD drawing of the e-gun. The most important components are highlighted. (<b>Right</b>): COMSOL simulation of the electron beam produced with the e-gun.</p>
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<p>(<b>Top</b>): measurement of the e-gun beam spot performed with the Pixet. A beam size of ∼0.5 mm and a rate <math display="inline"><semantics> <msup> <mn>10</mn> <mn>4</mn> </msup> </semantics></math> electrons/s were found. (<b>Bottom</b>): measurement of a 10 keV electron spectrum acquired with an SDD. Only the central part of the pixel was hit with the e-gun beam. The best fit of the spectrum done with the detector model is also shown.</p>
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<p>CAD schematics of the setup used in the measurements. Section of source and detector (<b>top</b>), and side view (<b>bottom</b>).</p>
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<p>M1 Data acquired with the SDD main pixel in a 3-h measurement. The energy of the X-ray peaks and the tag of the different IC electrons are shown.</p>
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<p>Data-MC comparison for different values of the effective Mylar thickness (<b>top</b>). Reduced <math display="inline"><semantics> <msup> <mi>χ</mi> <mn>2</mn> </msup> </semantics></math> as a function of the effective Mylar thickness (<b>bottom</b>). The best-fit value of 7.2 μm is extracted through a parabolic fit.</p>
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<p>Best fit of MC prediction to the data set acquired with the <sup>109</sup>Cd source in vacuum. The fit is done only in the non-shaded area.</p>
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<p>Comparison of MC prediction to the dataset acquired with the <sup>109</sup>Cd source in air. The comparison is done only in the non-shaded area.</p>
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<p>Data acquired with the main SDD in a 6 h measurement using a <sup>14</sup>C source (<b>top</b>). <math display="inline"><semantics> <msup> <mi>χ</mi> <mn>2</mn> </msup> </semantics></math> as a function of the effective Mylar thickness for the two models: the Fermi theory prediction and the one including the experimental shape factor (<b>bottom</b>). The best fit for the effective Mylar thickness is 4.5 μm.</p>
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<p>Fit to the data set acquired with the <sup>14</sup>C source in vacuum using the MC prediction. The fit is performed only in the non-shaded area. The theoretical input is also shown.</p>
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<p>Fits obtained by varying <math display="inline"><semantics> <mi>λ</mi> </semantics></math> (<b>top</b>), the baseline resolution <math display="inline"><semantics> <mi>σ</mi> </semantics></math> (<b>center</b>) and the charge cloud width in Si (<b>bottom</b>).</p>
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<p>Fits obtained by varying <math display="inline"><semantics> <mi>λ</mi> </semantics></math> (<b>top</b>), the baseline resolution <math display="inline"><semantics> <mi>σ</mi> </semantics></math> (<b>center</b>) and the charge cloud width in Si (<b>bottom</b>).</p>
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<p>Fits obtained by varying the production cut for secondaries in GEANT4 (<b>top</b>) or the physics list used (<b>bottom</b>) in the simulations.</p>
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20 pages, 6204 KiB  
Article
Online Monitoring Method for Opening and Closing Time of 10 kV Spring Energy Storage Circuit Breaker Based on Transient Electrical Signal Characteristic Point Marking and Self-Calibration
by Liting Weng, Jiangtao Xiao, Zhaochuang Zhang, Jingang Wang, Yuchuan Wen, Fan Zhang, Xingyu Zhang, Lingyi Ma and Pengcheng Zhao
Energies 2024, 17(24), 6436; https://doi.org/10.3390/en17246436 - 20 Dec 2024
Viewed by 306
Abstract
Among all circuit breaker faults, mechanical failures account for a considerable proportion, and online monitoring of their mechanical characteristics is of great practical significance. The opening and closing time is a very important feature of the mechanical characteristics of the circuit breaker. Online [...] Read more.
Among all circuit breaker faults, mechanical failures account for a considerable proportion, and online monitoring of their mechanical characteristics is of great practical significance. The opening and closing time is a very important feature of the mechanical characteristics of the circuit breaker. Online monitoring of the opening and closing time of the circuit breaker has always been the focus and difficulty of the intelligent technology of switchgear. In this paper, for a 10 kV spring energy storage vacuum circuit breaker, transient voltage and current signals are innovatively used to calibrate the opening time, breaking time, and closing time, and an online monitoring method for the opening and closing time of a vacuum circuit breaker based on transient electrical signals is proposed. An online monitoring platform was built and a multi-group closing test was carried out to simulate the power plant environment. The opening and closing time samples of a spring energy storage vacuum circuit breaker were measured and compared with the measurement results of the mechanical properties tester. The comparison results show that this method has good stability, and the calculation error is controlled within 1% after self-calibration, which provides a new idea for the online monitoring research of the mechanical characteristics of spring energy storage vacuum circuit breakers. Full article
(This article belongs to the Special Issue Reliability of Power Electronics Devices and Converter Systems)
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<p>Timing diagram of the opening transient electrical signal and the moving contact travel curve.</p>
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<p>Timing diagram of closing transient electrical signal and moving contact travel curve.</p>
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<p>Waveform and time point calibration of transient electrical signals (voltage, current) when closing the circuit breaker.</p>
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<p>Waveform and time point calibration of transient electrical signals (voltage, current) during opening.</p>
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<p>Online monitoring system architecture diagram.</p>
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<p>Signal acquisition flow chart.</p>
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<p>Circuit breaker mechanical characteristics tester test wiring diagram.</p>
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<p>Compensation Flowchart.</p>
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<p>Error compensation iterative learning flow chart.</p>
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<p>Test the selected circuit breaker.</p>
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<p>Online monitoring system.</p>
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<p>Voltage and current waveforms.</p>
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<p><span class="html-italic">U</span><sub>N</sub> = 10 kV, <span class="html-italic">I</span>n = 13 A. Transient voltage and current waveforms in opening and closing test: (<b>a</b>) Closing waveform, (<b>b</b>) Opening waveform.</p>
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<p><span class="html-italic">U</span><sub>N</sub> = 10 kV, <span class="html-italic">I</span>n = 20 A. Transient voltage and current waveforms in opening and closing test: (<b>a</b>) Closing waveform, (<b>b</b>) Opening waveform.</p>
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<p><span class="html-italic">U</span><sub>N</sub> = 10 kV, <span class="html-italic">I</span>n = 27 A. Transient voltage and current waveforms in opening and closing test: (<b>a</b>) Closing waveform, (<b>b</b>) Opening waveform.</p>
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<p><span class="html-italic">U</span><sub>N</sub> = 10 kV, <span class="html-italic">I</span>n = 34 A. Transient voltage and current waveforms in opening and closing test: (<b>a</b>) Closing waveform, (<b>b</b>) Opening waveform.</p>
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<p>Opening and closing stroke–time curve: (<b>a</b>) Closing stroke curve, (<b>b</b>) Opening stroke curve.</p>
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<p>Normal distribution curve of opening and closing time error.</p>
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<p>Opening and closing time error compensation: (<b>a</b>) Closing time error compensation, (<b>b</b>) Opening time error compensation.</p>
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17 pages, 2033 KiB  
Article
Properties of Components of Renewable Motor Fuel Based on Plant Oils and Assessment of Their Compatibility with Traditional Fuels
by Sergii Boichenko, Anna Yakovlieva, Stepan Zubenko, Sergii Konovalov, Iryna Shkilniuk, Artem Artyukhov, Bogdan Wit, Krzysztof Czarnocki and Tomasz Wołowiec
Energies 2024, 17(24), 6390; https://doi.org/10.3390/en17246390 - 19 Dec 2024
Viewed by 391
Abstract
The growing demand for sustainable and environmentally friendly fuels and the increasing need to diversify energy sources have stimulated significant research in the field of renewable motor fuels. Despite the progress made, there is still a need to expand the feedstocks, optimize technological [...] Read more.
The growing demand for sustainable and environmentally friendly fuels and the increasing need to diversify energy sources have stimulated significant research in the field of renewable motor fuels. Despite the progress made, there is still a need to expand the feedstocks, optimize technological pathways, and, in particular, conduct comprehensive studies of the compatibility of renewable components with traditional fuels. In light of the above, the authors propose optimizing the properties of renewable fuels by using new vegetable oils and alcohols for their synthesis. The work is focused on studying the basic physical–chemical properties of fatty acid esters and assessing the possibility of using them as renewable components of motor fuels. Renewable components were obtained via the esterification of selected plant oils (rapeseed oil, camelina oil, palm kernel oil, and coconut oil) with different alcohols (ethanol and isobutanol) with further vacuum distillation of esters. The influence of the structure and composition of renewable components on their physical–chemical properties was studied and substantiated. It shows how the carbon number distribution and double bonds in fatty acid radicals influence the properties of renewable components. The paper shows the impact of the type and structure of alcohol used for esterification on the properties of studied products. The regularities in the change in properties of renewable components depending on the composition of oils and alcohols are explained and substantiated from the point of view of physical chemistry and the basics of forces of intermolecular interactions. Renewable components were compared to the properties of conventional motor fuels (diesel fuel and jet fuel). Based on the level of component compatibility with petroleum fuels, recommendations for replacing or blending petroleum fuels with renewable components were proposed. Full article
(This article belongs to the Special Issue Biomass, Biofuels and Waste: 3rd Edition)
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<p>Flowchart of synthesis of ethyl esters.</p>
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<p>Flowchart of synthesis of isobutyl esters.</p>
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<p>Fatty acid composition of plant oil esters, % (mas.).</p>
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<p>The density of plant oil esters at 15 °C, kg/m<sup>3</sup>.</p>
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<p>The viscosity of plant oil esters at 20 °C, mm<sup>2</sup>/s.</p>
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<p>The viscosity of plant oil esters as a function of temperature.</p>
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<p>The freezing point of plant oil esters, °C.</p>
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16 pages, 6553 KiB  
Article
IR Pulsed Laser Ablation of Carbon Materials in High Vacuum
by Lorenzo Torrisi, Alfio Torrisi and Mariapompea Cutroneo
Appl. Sci. 2024, 14(24), 11744; https://doi.org/10.3390/app142411744 - 16 Dec 2024
Viewed by 438
Abstract
This work aimed to understand how the energy released by short laser pulses can produce different effects in carbon targets with different allotropic states. The IR pulse laser ablation, operating at 1064 nm wavelength, 3 ns pulse duration, and 100 mJ pulse energy, [...] Read more.
This work aimed to understand how the energy released by short laser pulses can produce different effects in carbon targets with different allotropic states. The IR pulse laser ablation, operating at 1064 nm wavelength, 3 ns pulse duration, and 100 mJ pulse energy, has been used to irradiate different types of carbon targets in a high vacuum. Graphite, highly oriented pyrolytic graphite, glassy carbon, active carbon, and vegetable carbon have exhibited different mass densities and have been laser irradiated. Time-of-flight (TOF) measurements have permitted the evince of the maximum carbon ion acceleration in the generated plasma (of about 200 eV per charge state) and the maximum yield emission (96 μg/pulse in the case of vegetal carbon) along the direction normal to the irradiated surface. The ion energy analyzer measured the carbon charge states (four) and their energy distributions. Further plasma investigations have been performed using a fast CCD camera image and surface profiles of the generated craters to calculate the angular emission and the ablation yield for each type of target. The effects as a function of the target carbon density and binding energy have been highlighted. Possible applications for the generation of thin films and carbon nanoparticles are discussed. Full article
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<p>Sketch of the experimental setup.</p>
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<p>ICR-TOF spectra relative to the six laser irradiated targets: HOPG (<b>a</b>), graphite (<b>b</b>), pencil graphite (<b>c</b>), glassy carbon (<b>d</b>), active carbon (<b>e</b>), and vegetable carbon (<b>f</b>).</p>
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<p>IEA-TOF spectra relative to graphite target analyzed to different E/z filter ratios: 100 eV/z (<b>a</b>), 200 eV/z (<b>b</b>), 400 eV/z (<b>c</b>), 600 eV/z (<b>d</b>), 800 eV/z (<b>e</b>), and 1000 eV/z (<b>f</b>).</p>
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<p>IEA measurements of C ion energy and charge state distributions.</p>
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<p>CCD image of the carbon plasma produced in 1 μs from the laser ablation of HOPG (<b>a</b>), graphite (<b>b</b>), pencil graphite (<b>c</b>), glassy carbon (<b>d</b>), active carbon (<b>e</b>), and vegetal graphite (<b>f</b>).</p>
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<p>IC-TOF spectra acquired using a laser ablation at 45° incidence angle of graphite target and at different angles of detection around the normal direction: 0° (<b>a</b>), 22° (<b>b</b>), 45° (<b>c</b>), and 60° (<b>d</b>).</p>
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<p>Carbon ion angular emission distribution in graphite, for yield (<b>a</b>), maximum energy (<b>b</b>), photon intensity (<b>c</b>), and comparison between yield emission from graphite and vegetable carbon target (<b>d</b>).</p>
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<p>Crater depth profiles of the six targets irradiated in the same experimental conditions: HOPG (<b>a</b>), graphite (<b>b</b>), pencil graphite (<b>c</b>), glassy carbon (<b>d</b>), active carbon (<b>e</b>), and vegetable carbon (<b>f</b>).</p>
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12 pages, 2738 KiB  
Article
Influence of Substrate Bias Voltage on Structure and Properties of (AlCrMoNiTi)N Films
by Xue Gao, Bin Li, Yiman Zhao, Xunwang Shi, Yujie Chen, Bin Liao and Erzhou Ren
Nanomaterials 2024, 14(24), 2002; https://doi.org/10.3390/nano14242002 - 13 Dec 2024
Viewed by 438
Abstract
(AlCrMoNiTi)N high-entropy alloy nitride (HEAN) films were synthesized at various bias voltages using the co-filter cathodic vacuum arc (co-FCVA) deposition technique. This study systematically investigates the effect of bias voltage on the microstructure and performance of HEAN films. The results indicate that an [...] Read more.
(AlCrMoNiTi)N high-entropy alloy nitride (HEAN) films were synthesized at various bias voltages using the co-filter cathodic vacuum arc (co-FCVA) deposition technique. This study systematically investigates the effect of bias voltage on the microstructure and performance of HEAN films. The results indicate that an increase in bias voltage enhances the energy of ions while concomitantly reducing the deposition rate. All synthesized (AlCrMoNiTi)N HEAN films demonstrated the composite structure composed of FCC phase and metallic Ni. The hardness of the (AlCrMoNiTi)N HEAN film synthesized at a bias voltage of −100 V attained a maximum value of 38.7 GPa. This high hardness is primarily attributed to the synergistic effects stemming from the formation of strong metal-nitrogen (Me-N) bonding formed between the target elements and the N element, the densification of the film structure, and the ion beam-assisted bombardment strengthening of the co-FCVA deposition technique. In addition, the corrosion current density of the film prepared at this bias voltage was measured at 4.9 × 10−7 A·cm−2, significantly lower than that of 304 stainless steel, indicating excellent corrosion resistance. Full article
(This article belongs to the Section Nanoelectronics, Nanosensors and Devices)
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<p>Schematic diagram of the co-FCVA equipment.</p>
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<p>Deposition rate of the (AlCrMoNiTi)N HEAN films as a function of the bias voltage.</p>
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<p>GIXRD patterns of (AlCrMoNiTi)N HEAN films prepared under various bias voltages.</p>
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<p>Surface morphology images of the (AlCrMoNiTi)N HEAN films obtained by AFM: (<b>a</b>) 0, (<b>b</b>) −100, (<b>c</b>) −150, (<b>d</b>) −200 and (<b>e</b>) −300 V.</p>
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<p>The cross-sectional FESEM images of the (AlCrMoNiTi)N HEAN films prepared at various bias voltage: (<b>a</b>) 0, (<b>b</b>) −100, (<b>c</b>) −150, (<b>d</b>) −200 and (<b>e</b>) −300 V.</p>
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<p>Mechanical properties of the (AlCrMoNiTi)N HEAN films fabricated at various bias voltages: (<b>a</b>) H and E, (<b>b</b>) H/E and H<sup>3</sup>/E<sup>2</sup> and (<b>c</b>) load-displacement curves.</p>
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<p>Nanoindentation FESEM images of the (AlCrMoNiTi)N HEAN films prepared under various bias voltages: (<b>a</b>) 0, (<b>b</b>) −100 and (<b>c</b>) −300 V.</p>
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<p>Potentiodynamic polarization curves of (AlCrMoNiTi)N HEAN films synthesized on the surface of 304 SS and 304 SS in 5 wt.% H<sub>2</sub>SO<sub>4</sub> solution.</p>
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20 pages, 11473 KiB  
Article
The Effect of Zirconium on the Microstructure and Properties of Cast AlCoCrFeNi2.1 Eutectic High-Entropy Alloy
by Rongbin Li, Weichu Sun, Saiya Li and Zhijun Cheng
Materials 2024, 17(23), 5938; https://doi.org/10.3390/ma17235938 - 4 Dec 2024
Viewed by 499
Abstract
To improve the performance of AlCoCrFeNi2.1 eutectic high-entropy alloys (EHEA) to meet industrial application requirements, ZrxAlCoCrFeNi2.1 high-entropy alloys (x = 0, 0.01, 0.05, 0.1) were synthesized through vacuum induction melting. Their microstructures were analyzed using X-ray diffraction (XRD), scanning [...] Read more.
To improve the performance of AlCoCrFeNi2.1 eutectic high-entropy alloys (EHEA) to meet industrial application requirements, ZrxAlCoCrFeNi2.1 high-entropy alloys (x = 0, 0.01, 0.05, 0.1) were synthesized through vacuum induction melting. Their microstructures were analyzed using X-ray diffraction (XRD), scanning electron microscopy (SEM), and energy-dispersive spectroscopy (EDS). Additionally, the hardness, low-temperature compressive properties, nanoindentation creep behavior, and corrosion resistance of these alloys were evaluated. The results showed that AlCoCrFeNi2.1 is a eutectic high-entropy alloy composed of FCC and B2 phases, with the FCC phase being the primary phase. The addition of Zr significantly affected the phase stability, promoting the formation of intermetallic compounds such as Ni7Zr2, which acted as a bridge between the FCC and B2 phases. Zr addition enhanced the performance of the alloy through solid-solution and dispersion strengthening. However, as the Zr content increased, Ni gradually precipitated from the B2 phase, leading to a reduction in the fraction of the B2 phase. Consequently, at x = 0.1, the microhardness and compressive strength decreased at room temperature. Furthermore, a higher Zr content reduced the sensitivity of the alloy to loading rate changes during creep. At x = 0.05, the creep exponent exceeded 3, indicating that dislocation creep mechanisms dominated. In the ZrxAlCoCrFeNi2.1 (where x = 0, 0.01, 0.05, 0.1) alloys, when the Zr content is 0.1, the alloy exhibits the lowest self-corrosion current density of 0.034197 μA/cm2 and the highest pitting potential of 323.06 mV, indicating that the alloy has the best corrosion resistance. Full article
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<p>XRD pattern of the as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> (x = 0, 0.01, 0.05, and 0.1) high-entropy alloys (<b>a</b>) XRD pattern; (<b>b</b>) (111) plane pattern; (<b>c</b>) line diagram of lattice parameters.</p>
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<p>SEM images of as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> alloys: (<b>a</b>,<b>b</b>) x = 0; (<b>c</b>,<b>d</b>) x = 0.01; (<b>e</b>,<b>f</b>) x = 0.05; (<b>g</b>,<b>h</b>) x = 0.1.</p>
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<p>EDS mapping of as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> alloys: (<b>a</b>) x = 0; (<b>b</b>) x = 0.01; (<b>c</b>) x = 0.05; (<b>d</b>) x = 0.1.</p>
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<p>(<b>a</b>) TEM bright field image and corresponding SAED patterns of the three phases in cast Zr<sub>0.1</sub>AlCoCrFeNi<sub>2.1</sub> alloy; (<b>b</b>) FCC phase TEM dark field image; (<b>c</b>) B2 phase TEM bright field image.</p>
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<p>The load-displacement curves of the cast state Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> alloy, with arrows indicating the pop-in phenomenon: (<b>a</b>) x = 0; (<b>b</b>) x = 0.01; (<b>c</b>) x = 0.05; (<b>d</b>) x = 0.1.</p>
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<p>Creep displacement–time curves of as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> HEAs: (<b>a</b>) x = 0; (<b>b</b>) x = 0.01; (<b>c</b>) x = 0.05; (<b>d</b>) = 0.1.</p>
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<p>Creep stress exponent fitting curve of as−cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> HEAs: (<b>a</b>) x = 0; (<b>b</b>) x = 0.01; (<b>c</b>) x = 0.05; (<b>d</b>) = 0.1.</p>
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<p>The relationship diagram of the hardness and lattice parameter of as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> HEAs with the change of Zr content.</p>
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<p>Room temperature stress–strain curves of as-cast Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub>high entropy alloys.</p>
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<p>Potentiodynamic polarization curves of Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> high entropy alloy in 3.5 wt% NaCl corrosion solution.</p>
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<p>EIS images of the Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> high entropy alloy in 3.5 wt% NaCl solution: (<b>a</b>) Nyquist plot and equivalent circuit diagram; (<b>b</b>) Bode plot.</p>
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<p>The surface pit morphology (in the boxes) and EDS line scan images (with the lines indicating the scan length) of the Zr<sub>x</sub>AlCoCrFeNi<sub>2.1</sub> high entropy alloy after corrosion in 3.5 wt% NaCl solution: (<b>a</b>,<b>a1</b>,<b>a2</b>) x = 0; (<b>b</b>,<b>b1</b>,<b>b2</b>) x = 0.01; (<b>c</b>,<b>c1</b>,<b>c2</b>) x = 0.05; (<b>d</b>,<b>d1</b>,<b>d2</b>) x = 0.1.</p>
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11 pages, 8288 KiB  
Article
Magnetic Performance and Anticorrosion Coating Stability of Thermally Demagnetized Nd-Fe-B Permanent Magnets for Reuse Applications
by Tomaž Tomše, Pierre Kubelka, Rosario Moreno López, Peter Fleissner, Laura Grau, Matej Zaplotnik and Carlo Burkhardt
Materials 2024, 17(23), 5927; https://doi.org/10.3390/ma17235927 - 4 Dec 2024
Viewed by 506
Abstract
Nd-Fe-B-type permanent magnets, containing approximately 30% critical rare-earth elements by weight, are essential components in renewable energy systems (e.g., wind turbines, hydroelectric generators) and electric vehicles. They are also critical for consumer electronics and electric motors in products like energy-efficient air conditioners and [...] Read more.
Nd-Fe-B-type permanent magnets, containing approximately 30% critical rare-earth elements by weight, are essential components in renewable energy systems (e.g., wind turbines, hydroelectric generators) and electric vehicles. They are also critical for consumer electronics and electric motors in products like energy-efficient air conditioners and home appliances. In light of advancing sustainability goals, the direct reuse of magnets from end-of-life devices offers a promising alternative to energy-intensive and costly recycling methods based on hydro- and pyrometallurgical processes, as well as modern short-loop recycling through hydrogen processing. However, Nd-Fe-B magnets must be demagnetized before they can be extracted from devices. This study explores the effects of thermal demagnetization, performed either in air or a vacuum, on the stability of anticorrosion coatings and the magnetic performance of remagnetized magnets. Corrosion tests were conducted to assess the compatibility of various coatings with thermal demagnetization, identifying those most suitable for future applications involving magnet reuse. Full article
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<p>DSC curves of the magnets with marked Curie temperatures (red circles) and small endothermic peaks attributed to the melting of the rare-earth-rich phase (arrows). The coatings were removed before the analysis.</p>
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<p>Second-quadrant demagnetization curves measured before and after thermal demagnetization (TD). (<b>a</b>) Zn-coated magnet measured at room temperature. (<b>b</b>) Ni/Cu/Ni-coated magnet measured at room temperature. (<b>c</b>) Epoxy-coated magnet measured at 100 °C.</p>
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<p>Backscattered-electron (BSE) mode SEM images of the polished cross-sections of Zn-coated samples with EDS mapping showing the distribution of Zn. (<b>a</b>) Before thermal demagnetization. (<b>b</b>) After thermal demagnetization in air. (<b>c</b>) After thermal demagnetization in a vacuum.</p>
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<p>(<b>a</b>) Higher-magnification backscattered-electron (BSE) mode SEM image close to the Nd-Fe-B/Zn interface on a Zn-coated magnet after thermal demagnetization in a vacuum with a marked area of the EDS linescan (yellow line). (<b>b</b>,<b>c</b>) Elemental composition of a matrix grain and the surrounding phase determined via EDS linescan analysis at a higher and lower scaling, respectively.</p>
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<p>Photographs of the magnet samples on millimeter paper. Before thermal demagnetization: (<b>a</b>) Ni/Cu/Ni-coated and (<b>b</b>) epoxy-coated. After thermal demagnetization in air: (<b>c</b>) Ni/Cu/Ni-coated and (<b>d</b>) epoxy-coated. After thermal demagnetization in vacuum: (<b>e</b>) Ni/Cu/Ni-coated and (<b>f</b>) epoxy-coated.</p>
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<p>Backscattered-electron (BSE) mode SEM images of the polished cross-sections of the Ni/Cu/Ni-coated samples with EDS mapping showing the distribution of Ni and Cu. (<b>a</b>) Before thermal demagnetization. (<b>b</b>) After thermal demagnetization in air. (<b>c</b>) After thermal demagnetization in a vacuum.</p>
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<p>Backscattered-electron (BSE) mode SEM images of the polished cross-sections of the epoxy-coated magnet samples with arrows marking the epoxy layer. (<b>a</b>) Before thermal demagnetization. (<b>b</b>) After thermal demagnetization in a vacuum.</p>
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<p>Photographs of the magnet samples on millimeter paper after corrosion tests. Before thermal demagnetization: (<b>a</b>) Ni/Cu/Ni-coated and (<b>b</b>) epoxy-coated. After thermal demagnetization in the air: (<b>c</b>) Ni/Cu/Ni-coated and (<b>d</b>) epoxy-coated. After thermal demagnetization in a vacuum: (<b>e</b>) Ni/Cu/Ni-coated and (<b>f</b>) epoxy-coated.</p>
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15 pages, 1604 KiB  
Review
Peniotron: A Promising Microwave Source with Potential That Has Yet to Be Realized
by Svilen Sabchevski
Appl. Sci. 2024, 14(23), 11246; https://doi.org/10.3390/app142311246 - 2 Dec 2024
Viewed by 591
Abstract
The peniotron is a fast-wave vacuum tube that can generate coherent microwave radiation in the millimeter-wave range. Although it uses a beam of gyrating electrons like other gyro-devices (gyrotron, gyro-TWT, gyro-BWO, etc.), its operating principle is completely different from that of electron cyclotron [...] Read more.
The peniotron is a fast-wave vacuum tube that can generate coherent microwave radiation in the millimeter-wave range. Although it uses a beam of gyrating electrons like other gyro-devices (gyrotron, gyro-TWT, gyro-BWO, etc.), its operating principle is completely different from that of electron cyclotron masers. The theory predicts a very high efficiency (about 95%) of the peniotron mechanism of interaction and energy transfer from the electron beam to the wave. However, this extremely attractive and advantageous property of peniotrons has not yet been realized in practice. In this paper, we present the current state of research on this class of devices and give an overview of the theory and experimental results of peniotrons and gyro-peniotrons with different configurations. We also discuss the main problems and the reasons for the lower efficiency and finally evaluate the potential for solving the problems and revitalizing the work on this promising device. Full article
(This article belongs to the Section Applied Physics General)
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<p>Two typical configurations of peniotron interaction circuits: (<b>a</b>) double-ridge waveguide peniotron and (<b>b</b>) <math display="inline"><semantics> <msub> <mi>TE</mi> <mn>11</mn> </msub> </semantics></math>—mode peniotron with a rectangular waveguide. Figures reproduced from [<a href="#B18-applsci-14-11246" class="html-bibr">18</a>] (copyright ©2016 IEICE).</p>
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<p>Circular interaction structures: (<b>a</b>) smooth-wall waveguide (cavity) used in gyropeniotrons with helical electron beams (<math display="inline"><semantics> <msub> <mi>R</mi> <mi>c</mi> </msub> </semantics></math>—cavity radius, <math display="inline"><semantics> <msub> <mi>R</mi> <mrow> <mi>g</mi> <mi>c</mi> </mrow> </msub> </semantics></math>—guiding center radius of gyrating electrons); (<b>b</b>,<b>c</b>) slotted (vane-loaded) waveguide and rising-sun cavity, respectively, used with uniaxial electron beams. Here, <span class="html-italic">a</span> and <span class="html-italic">b</span> are the inner and outer radius of the slots and <math display="inline"><semantics> <msub> <mi>r</mi> <mi>L</mi> </msub> </semantics></math> is the Larmor radius of the electron orbits.</p>
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<p>Asynchronism in the peniotron due to the fact that the electrons gyrate faster than the cyclotron resonance wave: (<b>a</b>) angular frequencies of the gyrating electrons and the rotating electromagnetic wave; (<b>b</b>) motion of the electron with respect to a coordinate system associated with the wave (in this example, <math display="inline"><semantics> <mrow> <mi>m</mi> <mo>=</mo> <mn>2</mn> </mrow> </semantics></math>); (<b>c</b>) the field amplitude that the electron “sees” at different moments (indicated by dots) during one cyclotron period.</p>
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<p>On the operating principle of peniotron. The guiding center of the electron orbit drifts in such a way as to bring the electron into a stronger field at the decelerating phase and conversely into a weaker field at the accelerating phase. The orbits of an initially accelerated and an initially decelerated electron are shown in the panes (<b>a</b>,<b>b</b>), respectively. Below them, the distribution of the electric field <math display="inline"><semantics> <msub> <mi>E</mi> <mi>y</mi> </msub> </semantics></math> in the vertical <span class="html-italic">Y</span> direction along the horizontal axis <span class="html-italic">X</span> is shown.</p>
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<p>Brillouin diagram for the case of electron cyclotron autoresonance.</p>
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<p>Azimuthal electric fields in the vanes of the circuit. Here, the azimuthal angle (0–360°) is linearly stretched.</p>
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<p>Example of concurrent research on LOG and gyro-peniotron development: (<b>a</b>) EOS of LOG with a permanent magnet (shown are a photo of the device, a drawing of the tube, and results from the ray-tracing analysis of the EOS); and (<b>b</b>) a rising-sun cavity of a peniotron (shown is the electric field distribution calculated by the computer program for the evaluation of RF SUPERFISH cavities [<a href="#B80-applsci-14-11246" class="html-bibr">80</a>]).</p>
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<p>Example of concurrent research on LOG and gyro-peniotron development: (<b>a</b>) EOS of LOG with a permanent magnet (shown are a photo of the device, a drawing of the tube, and results from the ray-tracing analysis of the EOS); and (<b>b</b>) a rising-sun cavity of a peniotron (shown is the electric field distribution calculated by the computer program for the evaluation of RF SUPERFISH cavities [<a href="#B80-applsci-14-11246" class="html-bibr">80</a>]).</p>
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