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Search Results (28,159)

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18 pages, 8070 KiB  
Article
Comparative Analysis of Dielectric Behavior under Temperature and UV Radiation Exposure of Insulating Paints for Electrical Equipment Protection—The Necessity of a New Standard?
by Alina Ruxandra Caramitu, Magdalena Valentina Lungu, Romeo Cristian Ciobanu, Mihaela Aradoaei, Eduard-Marius Lungulescu and Virgil Marinescu
Coatings 2024, 14(9), 1194; https://doi.org/10.3390/coatings14091194 - 16 Sep 2024
Abstract
This paper describes the behavior of some epoxy, acrylic and polyurethane paints used in the protection of electrical equipment under the action of different degradation factors. The degradation factors chosen were temperature and UV radiation. The behavior of the paints under the action [...] Read more.
This paper describes the behavior of some epoxy, acrylic and polyurethane paints used in the protection of electrical equipment under the action of different degradation factors. The degradation factors chosen were temperature and UV radiation. The behavior of the paints under the action of these factors was interpreted by the variation of the tangent of the dielectric loss angle (tg Delta) as well as by FTIR and TG DSC analyses. Tg Delta was considered the reference dielectric characteristic because it best simulates the functionality of the material. The results presented in this paper lead to the conclusion that exposure to thermal cycles and UV radiation is necessary for each paint to give indications about their possibility of use in these conditions. At the same time, the evaluation of thermal stability, even if the exposure is at lower temperatures (than those at which we performed the tests) and/or for shorter periods, is very important for placing the paint in an insulation class. The tests that were the subject of this work provide us with the following information about the three types of paints analyzed: the highest resistance to thermal cycles is presented by S3, followed by S2 and then S1; thermal endurance tests place the polyurethane paint (S3) in insulation class E and the epoxy paint (S1) in insulation class B; and the tests to determine resistance to UV radiation qualify the best paint as acrylic (S2) and the worst as polyurethane (S3). Thus, it can be said that in applications where it is necessary for the protective film to withstand high temperatures, the use of S3 paint (polyurethane) is recommended, and in applications where the films are kept under the influence of UV radiation for a longer time, it is recommended to use coded paint S2 (acrylic). The results presented in this paper lead to the conclusion that the exposure to thermal cycles simulating the use in outdoor conditions and the resilience of paints under UV radiation conditions must be performed for each paint according to its specific use, and the dielectric characteristics must be carefully evaluated because they can reach values under the accepted limit—e.g., thermal stability evaluation—even if the exposure is at lower temperatures and/or for shorter periods. The conclusions of the experimental work must be generalized at different types of electrical insulating paints, and maybe a new standard is necessary to assess the paints’ behavior under usage conditions, with the paints needing to be treated separately from the classical polymeric insulation systems. Full article
(This article belongs to the Special Issue Surface Modification and Coating Techniques for Polymers)
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<p>The diagram of the thermal cycling test.</p>
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<p>X-ray diffractogram for S1.</p>
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<p>X-ray diffractogram for S2.</p>
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<p>X-ray diffractogram for S3.</p>
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<p>Spectral data for sample S1.</p>
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<p>Spectral data for sample S2.</p>
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<p>Spectral data for sample S3.</p>
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<p>TG-DSC curves for S1 initial and UV-irradiated samples after 92 h.</p>
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<p>TG-DSC curves for the S2 initial and UV-irradiated samples after 92 h.</p>
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<p>DTG curves for the S3 initial and UV-irradiated samples after 92 h.</p>
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<p>Dielectric features of S1.</p>
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<p>Dielectric features of S2.</p>
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<p>Dielectric features of S3.</p>
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<p>Tg Delta characteristics vs. exposure time for S1.</p>
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<p>Tg Delta characteristics vs. exposure time for S2.</p>
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<p>Tg Delta characteristics vs. exposure time for S3.</p>
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<p>Variation of tg Delta vs. duration of thermal exposure at 100 °C: (<b>a</b>) S1; (<b>b</b>) S3.</p>
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<p>Variation of tg Delta vs. duration of thermal exposure at 200 °C: (<b>a</b>) S1; (<b>b</b>) S3.</p>
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<p>Variation of tg Delta vs. duration of thermal exposure at 250 °C: (<b>a</b>) S1; (<b>b</b>) S3.</p>
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<p>Thermal stability of electrical insulating paints: (<b>a</b>) S1-epoxy; (<b>b</b>) S3-polyurethane.</p>
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22 pages, 326 KiB  
Article
Die Politik von Caligari: Totalitarian Anxieties in Adaptations of Robert Weine’s Das Cabinet des Dr. Caligari
by Phillip Louis Zapkin
Humanities 2024, 13(5), 119; https://doi.org/10.3390/h13050119 - 16 Sep 2024
Abstract
Contemporary politics is filled with anxiety about the survival of democracy—particularly within a framework pitting liberal representative democracy against authoritarianism. In times of anxiety about authoritarianism, Western artists repeatedly return to a masterpiece of relatively early cinema: Robert Weine’s silent film Das Cabinet [...] Read more.
Contemporary politics is filled with anxiety about the survival of democracy—particularly within a framework pitting liberal representative democracy against authoritarianism. In times of anxiety about authoritarianism, Western artists repeatedly return to a masterpiece of relatively early cinema: Robert Weine’s silent film Das Cabinet des Dr. Caligari, or The Cabinet of Dr. Caligari. This essay examines three twenty-first century adaptations: David Lee Fisher’s 2005 remake of the film; James Morrow’s 2017 novel, The Asylum of Dr. Caligari; and Georgie Bailey’s 2022 play Caligari. I argue that while the direct politico-cultural anxieties of Weine’s film have often been overstated, the emergence of adaptations during periods of heightened concern about authoritarianism reflects a deep-seated reception of the film as anticipating autocratic governance. However, for all its fears about power, control, and the loss of self-determination, Weine’s movie also contains the seeds of liberation. Cesare ultimately sacrifices his own life rather than murdering Jane. And it is this gesture that the adaptations examined here seek—a gesture of resistance. The sleepwalker can awaken and assert a form of just resistance in the world, even if the penalties are steep. Full article
(This article belongs to the Special Issue Re-imagining Classical Monsters)
14 pages, 2778 KiB  
Article
Enhancing Long-Term Memory in Carbon-Nanotube-Based Optoelectronic Synaptic Devices for Neuromorphic Computing
by Seung Hun Lee, Hye Jin Lee, Dabin Jeon, Hee-Jin Kim and Sung-Nam Lee
Nanomaterials 2024, 14(18), 1501; https://doi.org/10.3390/nano14181501 - 16 Sep 2024
Abstract
This study investigates the impact of spin-coating speed on the performance of carbon nanotube (CNT)-based optoelectronic synaptic devices, focusing on their long-term memory properties. CNT films fabricated at lower spin speeds exhibited a greater thickness and density compared to those at higher speeds. [...] Read more.
This study investigates the impact of spin-coating speed on the performance of carbon nanotube (CNT)-based optoelectronic synaptic devices, focusing on their long-term memory properties. CNT films fabricated at lower spin speeds exhibited a greater thickness and density compared to those at higher speeds. These denser films showed enhanced persistent photoconductivity, resulting in higher excitatory postsynaptic currents (EPSCs) and the prolonged retention of memory states after UV stimulation. Devices coated at a lower spin-coating speed of 2000 RPM maintained EPSCs above 70% for 3600 s, outperforming their higher-speed counterparts in long-term memory retention. Additionally, the study demonstrated that the learning efficiency improved with repeated UV stimulation, with fewer pulses needed to achieve the maximum EPSC in successive learning cycles. These findings highlight that optimizing spin-coating speeds can significantly enhance the performance of CNT-based synaptic devices, making them suitable for applications in neuromorphic computing and artificial neural networks requiring robust memory retention and efficient learning. Full article
(This article belongs to the Special Issue Optical Composites, Nanophotonics and Metamaterials)
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Figure 1
<p>(<b>a</b>) Photographs of CNT/glass made by difference in spin-coating speed of CNT aqueous solution, (<b>b</b>) optical transmittance by CNT device manufactured according to spin-coating speed, (<b>c</b>) micro-surface shape images of CNT devices measured using an atomic force microscope, and (<b>d</b>) relative density graph of CNT devices.</p>
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<p>(<b>a</b>) Raman spectra of CNT film showing the RBM (green region), D (gray region), G<sup>−</sup>(pink region), G (yellow region), and G‘ (light peach color region) peaks under varying spin-coating speeds. (<b>b</b>) Normalized intensity of G and D/G peak ratio CNT film as a function of the spin-coating speed. (<b>c</b>) The area ratio of G<sup>−</sup>/G peaks and the normalized intensity of G<sup>−</sup> peaks of CNT film as a function of the spin-coating speed.</p>
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<p>(<b>a</b>) Dark current, (<b>b</b>) UV current, and (<b>c</b>) photocurrent of Au/CNT/Au devices with spin-coating speeds ranging from 2000 to 5000 RPM. The inserts in (<b>a</b>−<b>c</b>) show the dark current, UV current, and photocurrent measured at 1.0 V as functions of the spin-coating speed of the CNT film, respectively. (<b>d</b>) The variation in photocurrent over time for an Au/CNT/Au device coated at 2000 RPM, which is subjected to 365 nm UV light for 20 s, followed by 20 s of no irradiation, with the cycle repeated five times.</p>
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<p>Energy band diagram of an Au/CNT/Au optoelectronic synaptic device under (<b>a</b>) dark state with an applied voltage of 0 V and (<b>b</b>) UV-exposed state with an applied voltage of 1.0 V. (<b>c</b>) Schematic representation of an Au/CNT/Au optoelectronic synaptic device fabricated on glass substrate, illustrating the transmission of presynaptic and postsynaptic signals at the synapse upon UV application. The CNT-based optoelectronic synaptic device was coated at 2000 to 5000 RPM, (<b>d</b>) time-dependent variation of EPSC at 1.0 V when UV was applied in two consecutive light pulses with 0.5 s exposure and 0.5 s off time, and (<b>e</b>) PPF variation with increasing light off time (Δt) with a constant 0.5 s pulse exposure time.</p>
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<p>EPSCs as a function of time for Au/CNT/Au optoelectronic synaptic devices coated using spin-coating speeds of (<b>a</b>–<b>d</b>) 2000 RPM and (<b>e</b>–<b>h</b>) 5000 RPM, with varying (<b>a</b>,<b>e</b>) UV power, (<b>b</b>,<b>f</b>) exposure time, (<b>c</b>,<b>g</b>) exposure frequency, and (<b>d</b>,<b>h</b>) exposure numbers.</p>
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<p>The measured learning and forgetting experience behaviors in response to optical stimuli for CNT-based optoelectronic synaptic devices manufactured at (<b>a</b>) 2000 RPM and (<b>b</b>) 5000 RPM. A pulsed optical stimulus (365 nm UV light with a pulse width of 0.5 s and a 50% duty cycle) was applied 100 times to induce first learning, followed by two cycles of forgetting after turning off the UV light. To form human visual memory, nine devices were selected to visually represent the forgetting process after the first and the second learning processes, aiming to mimic human visual memory.</p>
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23 pages, 6574 KiB  
Review
Polymer Capacitor Films with Nanoscale Coatings for Dielectric Energy Storage: A Review
by Liang Cao, Rui Xi, Chen Zhou, Gaohui He, Feng Yang, Lingna Xu and He Li
Coatings 2024, 14(9), 1193; https://doi.org/10.3390/coatings14091193 - 15 Sep 2024
Viewed by 321
Abstract
Enhancing the energy storage properties of dielectric polymer capacitor films through composite materials has gained widespread recognition. Among the various strategies for improving dielectric materials, nanoscale coatings that create structurally controlled multiphase polymeric films have shown great promise. This approach has garnered considerable [...] Read more.
Enhancing the energy storage properties of dielectric polymer capacitor films through composite materials has gained widespread recognition. Among the various strategies for improving dielectric materials, nanoscale coatings that create structurally controlled multiphase polymeric films have shown great promise. This approach has garnered considerable attention in recent years due to its effectiveness. This review examines surface-coated polymer composites used for dielectric energy storage, discussing their dielectric properties, behaviors, and the underlying physical mechanisms involved in energy storage. The review thoroughly examines the fabrication methods for nanoscale coatings and the selection of coating materials. It also explores the latest advancements in the rational design and control of interfaces in organic–inorganic, organic–organic, and heterogeneous multiphase structures. Additionally, the review delves into the structure–property relationships between different interfacial phases and various interface structures, analyzing how nanoscale coatings the impact dielectric constant, breakdown strength, conduction and charge transport mechanisms, energy density and efficiency, thermal stability, and electrothermal durability of polymeric capacitor films. Moreover, the review summarizes relevant simulation methods and offers computational insights. The potential practical applications and characteristics of such nanoscale coating techniques are discussed, along with the existing challenges and practical limitations. Finally, the review concludes with a summary and outlook, highlighting potential research directions in this rapidly evolving field. Full article
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<p>(<b>a</b>) Applications of dielectric energy storage capacitors in areas of wind and solar power, electric vehicles, electrified aircrafts, and space shuttles. (<b>b</b>) Comparison of power density and energy density among energy storage devices including film capacitors, batteries, electrochemical capacitors, and fuel cells. (<b>c</b>) Scheme of charging (blue line) and discharging (red line) processes in dielectric energy storage capacitors, in which the gray area represents energy loss <span class="html-italic">U</span><sub>l</sub> and the orange area represents <span class="html-italic">U</span><sub>d</sub>.</p>
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<p>Schematic of (<b>a</b>) electronic breakdown, (<b>b</b>) electromechanical breakdown, (<b>c</b>) thermal breakdown, (<b>d</b>) charge injection (representative of the Schottky injection), and (<b>e</b>) charge migration (representative of the hopping conduction) processes.</p>
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<p>Schematic of chemical methods including (<b>a</b>) CVD (reused with permission, [<a href="#B73-coatings-14-01193" class="html-bibr">73</a>] © 2018, WILEY-VCH Verlag GmbH &amp; Co. KGaA), (<b>b</b>) ALD (reused with permission, [<a href="#B74-coatings-14-01193" class="html-bibr">74</a>] © 2024, Springer Nature), and (<b>c</b>) in situ (reused with permission, [<a href="#B75-coatings-14-01193" class="html-bibr">75</a>] © 2022, Springer Nature) growing methods for deposition.</p>
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<p>(<b>a</b>) Cross-sectional SEM image displaying the coating layers on a polymer film. (<b>b</b>) Electric field distortion in both uncoated PP and SiO<sub>2</sub>-coated PP films, as measured by the pulsed electroacoustic (PEA) method at 120 °C and 100 MV·m<sup>−1</sup>. (<b>c</b>) <span class="html-italic">η</span> and <span class="html-italic">U</span><sub>d</sub> of BOPP and BOPP-SiO<sub>2</sub> films with 180 nm coatings on both sides, evaluated at 120 °C. (<b>d</b>) <span class="html-italic">η</span> of different dielectric films before and after coating, tested at 150 °C (reused with permission, [<a href="#B73-coatings-14-01193" class="html-bibr">73</a>] © 2018, WILEY-VCH Verlag GmbH &amp; Co. KGaA). (<b>e</b>) Energy band diagrams showing the interfaces between metal electrodes and various deposited layers. (<b>f</b>) Diagram illustrating the sandwich structure and corresponding equivalent circuit. (<b>g</b>) Schematic of Schottky emission, where <span class="html-italic">ϕ</span><sub>B</sub> represents the electron potential barrier and LUMO denotes the lowest unoccupied molecular orbital. (<b>h</b>) Energy diagram illustrating the reduction in potential barrier due to image forces and applied electric fields (reused with permission, [<a href="#B76-coatings-14-01193" class="html-bibr">76</a>] © 2021, Elsevier). (<b>i</b>) Cross-sectional SEM images of nanolaminates with varying layer counts and 10 nm PEI interlayers. Pink areas represent Al<sub>2</sub>O<sub>3</sub>, and blue areas represent PEI. The scale bar is 50 nm in all images. (<b>j</b>) Optical photograph (left) of a 7-layer nanolaminate on a flexible substrate, with cross-sectional SEM images showing the nanolaminate under bending (middle) and a magnified view (right). The scale bar is 1 cm for the left image, 400 μm for the middle, and 200 nm for the right. (<b>k</b>) Schematic of a metal wire-based nanolaminate capacitor, with an optical photograph comparing it to commercial metalized PP and PET capacitors (reused with permission, [<a href="#B74-coatings-14-01193" class="html-bibr">74</a>] © 2021, Elsevier).</p>
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<p>Schematic of physical methods including (<b>a</b>) PVD (reused with permission, [<a href="#B80-coatings-14-01193" class="html-bibr">80</a>] © 2022 John Wiley &amp; Sons Australia, Ltd.; [<a href="#B81-coatings-14-01193" class="html-bibr">81</a>] © 2019, Elsevier) and (<b>b</b>) spraying and hot pressing (reused with permission, [<a href="#B82-coatings-14-01193" class="html-bibr">82</a>] © 2020, Elsevier) methods for deposition.</p>
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<p>(<b>a</b>) Flow chart of preparation of sandwich structure film; working principal diagram of surface h-BN functional layer. (<b>b</b>) A schematic representation of a real capacitor with a height of H = 40 mm and a diameter of D = 40 mm made by winding BN/PC/BN nanocomposite films. Internal temperature distribution when the ambient temperature is 80 °C, operating at an applied electric field of 100 MV/m in different capacitors made by composite films of PC/BN composites (reused with permission, [<a href="#B82-coatings-14-01193" class="html-bibr">82</a>] © 2020, Elsevier). (<b>c</b>) Schematic illustration of the fabrication process of sandwich-structured nanocomposite films. (<b>d</b>) Comparison of <span class="html-italic">U</span><sub>d</sub> and <span class="html-italic">η</span> (reused with permission, [<a href="#B93-coatings-14-01193" class="html-bibr">93</a>] © 2023, Elsevier).</p>
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<p>Schematic of molecular-level surface modification methods for deposition, represented by irradiation (reused with permission, [<a href="#B66-coatings-14-01193" class="html-bibr">66</a>] © 2024, John Wiley &amp; Sons).</p>
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<p>(<b>a</b>) Energy levels, LUMO, and HOMO for pristine PP and PP with carbonyl. (<b>b</b>) <span class="html-italic">U</span><sub>d</sub> and (<b>c</b>) <span class="html-italic">η</span> versus electric field for pristine BOPP and <span class="html-italic">γ</span>-irradiated BOPP films (reused with permission, [<a href="#B96-coatings-14-01193" class="html-bibr">96</a>] © 2024, John Wiley &amp; Sons). (<b>d</b>) The schematic drawing of the preparation of the irradiated dielectric film. The filter is used to select ultraviolet (UV) rays with different frequencies, leading to the formation of free radicals in the shallow surface of polymer films after UV irradiation. The free radicals trap injected charges, accordingly, suppressing the electric field at the electrode–dielectric interface and inhibiting further charge injection. (<b>e</b>) Molecular structure and highest occupied molecular orbital (HOMO)/lowest unoccupied molecular orbital (LUMO) energy levels of the repeating unit of PEI and repeating unit of PEI with free radicals; the right axis represents the relative energy level in a vacuum. (<b>f</b>) Comparison of the <span class="html-italic">U</span><sub>d</sub> at <span class="html-italic">η</span> ≈ 90% between the pristine polymer dielectrics and irradiated polymer dielectrics at 150 and 200 °C (reused with permission, [<a href="#B99-coatings-14-01193" class="html-bibr">99</a>] © 2024, John Wiley &amp; Sons).</p>
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<p>Schematic of (<b>a</b>) polymeric coating in polymer composites, in which coated layer embedded with nanoparticles (green colored circles) could effectively impede dielectric breakdown pathway. [<a href="#B62-coatings-14-01193" class="html-bibr">62</a>] © 2024 John Wiley &amp; Sons. Schematic of polymeric coating methods including (<b>b</b>) successive drop-casting (reused with permission, [<a href="#B112-coatings-14-01193" class="html-bibr">112</a>] © 2020, American Chemical Society), (<b>c</b>) hot pressing (reused with permission, [<a href="#B116-coatings-14-01193" class="html-bibr">116</a>] © 2022, Elsevier), (<b>d</b>) electrospinning (reused with permission, [<a href="#B117-coatings-14-01193" class="html-bibr">117</a>] © 2024, John Wiley &amp; Sons), and (<b>e</b>) dip coating (reused with permission, [<a href="#B118-coatings-14-01193" class="html-bibr">118</a>] © 2023, Elsevier) methods for deposition.</p>
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<p>(<b>a</b>) Schematic diagram of AFM-IR technology. (<b>b</b>) Optical image of the cross-section of the sandwiched film and the area selected for characterization (reused with permission, [<a href="#B120-coatings-14-01193" class="html-bibr">120</a>] © 2022, Elsevier). (<b>c</b>) Schematic of the fabrication of PS-<span class="html-italic">b</span>-P4VP(PDP)/ZrO<sub>2</sub> NP supramolecular nanocomposites. (<b>d</b>) Simulated leakage current distributions of the ordered and disordered PS-<span class="html-italic">b</span>-P4VP(PDP) nanocomposites with 9 vol% ZrO<sub>2</sub> NPs under an applied electric field of 200 MV m<sup>−1</sup> (reused with permission, [<a href="#B62-coatings-14-01193" class="html-bibr">62</a>] © 2024, John Wiley &amp; Sons). (<b>e</b>) The incomplete breakdown in sandwich BaTiO<sub>3</sub>/PVDF nanocomposites at the applied voltage of 9 kV simulated using the finite element method (reused with permission, [<a href="#B121-coatings-14-01193" class="html-bibr">121</a>] © 2024, John Wiley &amp; Sons).</p>
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16 pages, 12097 KiB  
Article
Insight into the Structural and Performance Correlation of Photocatalytic TiO2/Cu Composite Films Prepared by Magnetron Sputtering Method
by Kun Lu, Miao Sun, Yaohong Jiang, Xinmeng Wu, Lijun Zhao and Junhua Xu
Catalysts 2024, 14(9), 621; https://doi.org/10.3390/catal14090621 - 14 Sep 2024
Viewed by 314
Abstract
Photocatalysis technology, as an efficient and safe environmentally friendly purification technique, has garnered significant attention and interest. Traditional TiO2 photocatalytic materials still face limitations in practical applications, hindering their widespread adoption. The research prepared TiO2/Cu films with different Cu contents [...] Read more.
Photocatalysis technology, as an efficient and safe environmentally friendly purification technique, has garnered significant attention and interest. Traditional TiO2 photocatalytic materials still face limitations in practical applications, hindering their widespread adoption. The research prepared TiO2/Cu films with different Cu contents using a magnetron sputtering multi-target co-deposition technique. The incorporation of Cu significantly enhances the antibacterial properties and visible light response of the films. The effects of different Cu contents on the microstructure, surface morphology, wettability, antibacterial properties, and visible light response of the films were investigated using an X-ray diffractometer, X-ray photoelectron spectrometer, field emission scanning electron microscope, confocal laser scanning microscope, Ultraviolet–visible spectrophotometer, and contact angle goniometer. The results showed that the prepared TiO2/Cu films were mainly composed of the rutile TiO2 phase and face-center cubic Cu phase. The introduction of Cu affected the crystal orientation of TiO2 and refined the grain size of the films. With the increase in Cu content, the surface roughness of the films first decreased and then increased. The water contact angle of the films first increased and then decreased, and the film exhibited optimal hydrophobicity when the Cu target power was 10 W. The TiO2/Cu films showed good antibacterial properties against Escherichia coli and Staphylococcus aureus. The introduction of Cu shifted the absorption edge of the films to the red region, significantly narrowed the band gap width to 2.5 eV, and broadened the light response range of the films to the visible light region. Full article
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<p>XRD patterns of TiO<sub>2</sub>/Cu composite films with different Cu target powers.</p>
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<p>XPS spectra of TiO<sub>2</sub>/Cu composite films with Cu target power of 15 W (<b>a</b>) full spectra. (<b>b</b>) Ti 2p. (<b>c</b>) Cu 2p and (<b>d</b>) O 1s.</p>
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<p>Surface morphology of TiO<sub>2</sub>/Cu composite films after annealing at 500 °C (<b>a</b>) TiO<sub>2</sub>; (<b>b</b>) Cu10; (<b>c</b>) Cu15; (<b>d</b>) Cu20.</p>
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<p>Laser confocal spectra of TiO<sub>2</sub>/Cu composite films with different Cu target powers (<b>a</b>) TiO<sub>2</sub>; (<b>b</b>) Cu10; (<b>c</b>) Cu15; (<b>d</b>) Cu20.</p>
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<p>Contact angle of TiO<sub>2</sub>/Cu films with different Cu target power (<b>a</b>) TiO<sub>2</sub>; (<b>b</b>) Cu10; (<b>c</b>) Cu15; (<b>d</b>) Cu20.</p>
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<p>Contact angle of TiO<sub>2</sub>/Cu films with different Cu target power.</p>
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<p>Antibacterial effect of TiO<sub>2</sub>/Cu composite film (<b>a</b>,<b>b</b>) <span class="html-italic">Escherichia coli</span>, (<b>c</b>,<b>d</b>) <span class="html-italic">Staphylococcus aureus</span>.</p>
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<p>(<b>a</b>) UV–Vis diffuse reflectance spectra and (<b>b</b>) optical band gap of TiO<sub>2</sub>/Cu composite films with different Cu target power.</p>
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<p>The antibacterial mechanism of TiO<sub>2</sub>/Cu composite film.</p>
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<p>Three-dimensional model of magnetron sputtering system.</p>
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<p>The schematic diagram of antibacterial test by coating plate method.</p>
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14 pages, 5815 KiB  
Article
The Evaluation and Analysis of the Anti-Corrosion Performance of the Sealing Material B72 for Metal Artifacts Based on Electrochemical Noise
by Hao Xu, Minghao Jia, Pei Hu, Shengyu Liu and Gang Hu
Coatings 2024, 14(9), 1190; https://doi.org/10.3390/coatings14091190 - 14 Sep 2024
Viewed by 257
Abstract
Paraloid B-72 (B72), as a transparent, colorless polymer material, has good film-forming ability when dissolved in acetone and is widely used as a sealing material for metal artifacts. In order to analyze and evaluate the preservation performance of B72 as a sealing material [...] Read more.
Paraloid B-72 (B72), as a transparent, colorless polymer material, has good film-forming ability when dissolved in acetone and is widely used as a sealing material for metal artifacts. In order to analyze and evaluate the preservation performance of B72 as a sealing material on the substrate of metal artifacts, a variety of electrochemical methods, mainly electrochemical noise (EN), and scanning electron microscopy (SEM) were applied to evaluate the B72 coating. The results showed that the B72 coating had a good preservation effect at the initial stage, and its poor water resistance led to the loss of its effectiveness after a few days of immersion. Compared with conventional electrochemical methods, electrochemical noise is non-destructive, which cannot cause new corrosion on the metal substrate and can well characterize the corrosion rate of the test system, and the results of its time domain and frequency domain analyses can correspond well with the polarization resistance and impedance spectra. Electrochemical noise is an effective method for evaluating the anti-corrosion performance of material preservation coatings. Full article
(This article belongs to the Special Issue New Trends in Conservation and Restoration of Cultural Heritage)
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<p>Different ways of coating the B72 film.</p>
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<p>(<b>a</b>) The salt bridge arrangement for ENM; (<b>b</b>) the arrangement for EIS and Polarization curves.</p>
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<p>Time records of (<b>a</b>) the potential and (<b>b</b>) the current of the blank group after de-trending.</p>
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<p>Time records of (<b>a</b>) the potential and (<b>b</b>) the current of the B72 group after de-trending.</p>
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<p>Polarization curves of (<b>a</b>) the blank group and (<b>b</b>) the B72 group at different immersion times.</p>
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<p>(<b>a</b>) <span class="html-italic">σ</span><sub>V</sub> and <span class="html-italic">σ</span><sub>I</sub> of the blank group at different immersion times; (<b>b</b>) <span class="html-italic">R</span><sub>n</sub> and <span class="html-italic">R</span><sub>p</sub> of the blank group at different immersion times.</p>
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<p>(<b>a</b>) <span class="html-italic">σ</span><sub>V</sub> and <span class="html-italic">σ</span><sub>I</sub> of the B72 group at different immersion times; (<b>b</b>) <span class="html-italic">R</span><sub>n</sub> and <span class="html-italic">R</span><sub>p</sub> of the B72 group at different immersion times.</p>
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<p>The blank group’s PSDs of (<b>a</b>) the current and (<b>b</b>) the potential, and (<b>c</b>) <span class="html-italic">Z</span><sub>n</sub> at different immersion times.</p>
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<p>The B72 group’s PSDs of (<b>a</b>) the current and (<b>b</b>) the potential, and (<b>c</b>) <span class="html-italic">Z</span><sub>n</sub> at different immersion times.</p>
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<p>The comparison of (<b>a</b>) the current PSD and (<b>b</b>) noise impedance <span class="html-italic">Z</span><sub>n</sub> of the two groups at different immersion times (0 d and 6 d).</p>
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<p>(<b>a</b>) Impedance modulus and (<b>b</b>) phase of the blank group at different immersion times.</p>
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<p>(<b>a</b>) Impedance modulus and (<b>b</b>) phase of the B72 group at different immersion times.</p>
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<p>The noise impedance <span class="html-italic">Z</span><sub>n</sub> with impedance modulus of (<b>a</b>) the blank group and (<b>b</b>) the B72 group at different immersion times.</p>
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<p>(<b>a</b>) The blank group and (<b>b</b>) the B72 group without immersion.</p>
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<p>(<b>a</b>) The blank group, (<b>b</b>) the pitting hole, and (<b>c</b>) the wrinkle of the B72 group after immersion.</p>
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<p>The scanning area and the elemental distribution of the B72 group.</p>
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9 pages, 4348 KiB  
Article
Surface Electronic Structure of Cr Doped Bi2Se3 Single Crystals
by Turgut Yilmaz, Xiao Tong, Zhongwei Dai, Jerzy T. Sadowski, Genda Gu, Kenya Shimada, Sooyeon Hwang, Kim Kisslinger, Elio Vescovo and Boris Sinkovic
Crystals 2024, 14(9), 812; https://doi.org/10.3390/cryst14090812 (registering DOI) - 14 Sep 2024
Viewed by 168
Abstract
Here, by using angle-resolved photoemission spectroscopy, we showed that Bi2−xCrxSe3 single crystals have a distinctly well-defined band structure with a large bulk band gap and undistorted topological surface states. These spectral features are unlike their thin film forms [...] Read more.
Here, by using angle-resolved photoemission spectroscopy, we showed that Bi2−xCrxSe3 single crystals have a distinctly well-defined band structure with a large bulk band gap and undistorted topological surface states. These spectral features are unlike their thin film forms in which a large nonmagnetic gap with a distorted band structure was reported. We further provide laser-based high resolution photoemission data which reveal a Dirac point gap even in the pristine sample. The gap becomes more pronounced with Cr doping into the bulk of Bi2Se3. These observations show that the Dirac point can be modified by the magnetic impurities as well as the light source. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
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<p>(<b>a</b>) The HAADF-STEM image of the Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub>. The inset figure is at a higher magnification. (<b>b</b>) The µLEED pattern of the sample taken with 25 eV electron energy. (<b>c</b>,<b>d</b>) Bi 5d, Se 3d, and Cr 2p core levels of Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub> sample at different depths. All of the data were collected at room temperature.</p>
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<p>(<b>a</b>) The total out-of-plane magnetic moment is given as a function of temperature for the ZFC and FC processes. During the measurements, 500 Oe is applied. (<b>b</b>) The total magnetic moment versus the applied field at 10 K, 100 K, and 150 K. The inset figure in (<b>b</b>) is the magnified hysteresis in the vicinity of the zero applied field.</p>
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<p>(<b>a</b>–<b>c</b>) ARPES maps of the Bi<sub>2</sub>Se<sub>3</sub>, Bi<sub>1.9</sub>Cr<sub>0.1</sub>Se<sub>3</sub>, and Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub> single crystals, respectively. Spectra were observed at 15 K with hv = 30 eV. The superimposed plots are the corresponding EDCs obtained along k<sub>x</sub> = 0 Å<sup>−1</sup>.</p>
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<p>(<b>a</b>–<b>d</b>) The hv-dependent experimental electronic structure of the Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub> single crystal obtained with hv = 30 eV, 40 eV, 50 eV, and 60 eV, respectively. The M-shaped white line in (<b>d</b>) represents the BVB. (<b>e</b>) The constant energy counters at various binding energy taken with hv = 50 eV. (<b>f</b>) The resonant valence band spectra of Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub> along the <math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <mi mathvariant="sans-serif">Γ</mi> </mrow> <mo>¯</mo> </mover> </mrow> </semantics></math>-point at the Cr 3p–3d edge. hv = 40 eV and hv = 50 eV are the off- and on-resonant hv, respectively.</p>
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<p>(<b>a</b>,<b>b</b>) ARPES maps of Bi<sub>2</sub>Se<sub>3</sub> and Bi<sub>1.78</sub>Cr<sub>0.22</sub>Se<sub>3</sub> single crystals, respectively. Spectra were recorded with hv = 6.3 eV laser energy at 12 K. EDCs taken along k<sub>‖</sub> = 0 Å<sup>−1</sup> are superimposed on each spectrum. Orange, pink, cyan, and green lines are Voight fitting profiles. Red and grey lines are overall fittings after Shirley backgrounds are subtracted.</p>
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13 pages, 4545 KiB  
Article
Comparison of Levitation Properties between Bulk High-Temperature Superconductor Blocks and High-Temperature Superconductor Tape Stacks Prepared from Commercial Coated Conductors
by Anke Kirchner, Tilo Espenhahn, Sebastian Klug, Kornelius Nielsch and Ruben Hühne
Materials 2024, 17(18), 4516; https://doi.org/10.3390/ma17184516 - 14 Sep 2024
Viewed by 184
Abstract
Bulk high-temperature superconductors (HTSs) such as REBa2Cu3O7−x (REBCO, RE = Y, Gd) are commonly used in rotationally symmetric superconducting magnetic bearings. However, such bulks have several disadvantages such as brittleness, limited availability and high costs [...] Read more.
Bulk high-temperature superconductors (HTSs) such as REBa2Cu3O7−x (REBCO, RE = Y, Gd) are commonly used in rotationally symmetric superconducting magnetic bearings. However, such bulks have several disadvantages such as brittleness, limited availability and high costs due to the time-consuming and energy-intensive fabrication process. Alternatively, tape stacks of HTS-coated conductors might be used for these devices promising an improved bearing efficiency due to a simplification of manufacturing processes for the required shapes, higher mechanical strength, improved thermal performance, higher availability and therefore potentially reduced costs. Hence, tape stacks with a base area of (12 × 12) mm2 and a height of up to 12 mm were prepared and compared to commercial bulks of the same size. The trapped field measurements at 77 K showed slightly higher values for the tape stacks if compared to bulks with the same size. Afterwards, the maximum levitation forces in zero field (ZFC) and field cooling (FC) modes were measured while approaching a permanent magnet, which allows the stiffness in the vertical and lateral directions to be determined. Similar levitation forces were measured in the vertical direction for bulk samples and tape stacks in ZFC and FC modes, whereas the lateral forces were almost zero for stacks with the REBCO films parallel to the magnet. A 90° rotation of the tape stacks with respect to the magnet results in the opposite behavior, i.e., a high lateral but negligible vertical stiffness. This anisotropy originates from the arrangement of decoupled superconducting layers in the tape stacks. Therefore, a combination of stacks with vertical and lateral alignment is required for stable levitation in a bearing. Full article
(This article belongs to the Special Issue Novel Superconducting Materials and Applications of Superconductivity)
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<p>Images of selected samples: (<b>a</b>) YBCO bulk; (<b>b</b>) tape stack prepared from GdBCO-coated conductors; (<b>c</b>) combination of stacks with different orientations to the magnetic field. The dimensions of all samples shown here are 12 mm × 12 mm × 8 mm.</p>
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<p>Schematic setup of the force measurement (<b>left</b>). The (<b>right</b>) panel shows the measurement procedure for vertical force measurement in zero field cooling (ZFC) and field cooling (FC) modes as well as for the different lateral force measurements.</p>
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<p>(<b>a</b>) Trapped field on the surface of the bulk and tape stack with a sample height of 8 mm; (<b>b</b>) Dependence of the maximum trapped field on the sample height. All data were measured at 77 K after magnetization at 3 T (closed symbols) and 0.35 T (open symbols). The lines are a visual guide.</p>
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<p>Vertical levitation force <span class="html-italic">F</span><sub>z</sub> at 77 K in ZFC mode for: (<b>a</b>) bulk samples and (<b>b</b>) tape stacks with different heights; (<b>c</b>) maximum levitation force <span class="html-italic">F</span><sub>z</sub> dependent on the sample height. The lines are a visual guide.</p>
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<p>Levitation forces for a vertical displacement ∆<span class="html-italic">z</span> = ±2 mm after FC at a distance <span class="html-italic">z</span><sub>0</sub> = 3 mm between permanent magnet and superconductor for bulk samples and tape stacks in parallel (<b>upper row</b>) or perpendicular (<b>lower row</b>) sample position. The values were measured at a temperature of 77 K.</p>
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<p>(<b>a</b>) Stiffness <span class="html-italic">dF</span>/<span class="html-italic">dz</span> for a vertical displacement ∆<span class="html-italic">z</span> = ±2 mm and (<b>b</b>) lateral stiffness <span class="html-italic">dF</span>/<span class="html-italic">dy</span> at a lateral displacement of ∆<span class="html-italic">z</span> = ±2.0 mm dependent on the sample height for bulk samples and tape stacks. The lines are a visual guide.</p>
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<p>Lateral forces for a lateral displacement ∆<span class="html-italic">z</span> = ± 5 mm after FC at a distance <span class="html-italic">z</span><sub>0</sub> = 2 mm between a permanent magnet and the superconductor for bulk samples and tape stacks in parallel (<b>upper row</b>) or perpendicular (<b>lower row</b>) sample position. The values were measured at a temperature of 77 K.</p>
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16 pages, 2186 KiB  
Article
Coeducation in Serial and Cinematographic Formats: Bibliometric Analysis on Web of Science (1986–2023)
by Simón Gil Tévar, Jose Javier Hueso Romero, Javier Gil Quintana and Eduardo García Blazquez
Educ. Sci. 2024, 14(9), 1007; https://doi.org/10.3390/educsci14091007 - 13 Sep 2024
Viewed by 363
Abstract
This study quantitatively examines the coeducation of television series and films between 1986 and 2023. This analysis has been facilitated by applying bibliometric analysis to scientific production using a relevant Web of Science (WoS) database. Analyses of 190 documents were conducted using quantitative [...] Read more.
This study quantitatively examines the coeducation of television series and films between 1986 and 2023. This analysis has been facilitated by applying bibliometric analysis to scientific production using a relevant Web of Science (WoS) database. Analyses of 190 documents were conducted using quantitative and descriptive methods. These results present a multifaceted analysis of scientific production, evaluating historical development, the productivity of countries and institutions, authors’ productivity, and sources’ productivity. The study indicates that scientific production has grown exponentially in the last decade; this coincides with the emergence of video-on-demand platforms, multiscreen consumption, and equality policies. The conclusions must emphasize the significant role played by fiction series and film productions as socializing agents and their educational potential. Full article
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<p>Flowchart of WoS sample sequencing. Own elaboration.</p>
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<p>Evolution of published scientific production (1986–2023). Own elaboration.</p>
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<p>Institutional network relating to co-authorship. Prepared by the authors using VOSviewer (2023).</p>
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<p>General co-authorship network and more prominent co-authorship networks. The authors prepared this figure using VOSviewer (2023).</p>
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<p>Co-citation network for authorship. Prepared by the authors using VOSviewer (2023).</p>
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<p>Cluster of influence. Own elaboration with CitNetExplorer (2023).</p>
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13 pages, 3446 KiB  
Article
Femtosecond Laser Ablation and Delamination of Functional Magnetic Multilayers at the Nanoscale
by Pavel Varlamov, Jan Marx, Yoav Urbina Elgueta, Andreas Ostendorf, Ji-Wan Kim, Paolo Vavassori and Vasily Temnov
Nanomaterials 2024, 14(18), 1488; https://doi.org/10.3390/nano14181488 - 13 Sep 2024
Viewed by 231
Abstract
Laser nanostructuring of thin films with ultrashort laser pulses is widely used for nanofabrication across various fields. A crucial parameter for optimizing and understanding the processes underlying laser processing is the absorbed laser fluence, which is essential for all damage phenomena such as [...] Read more.
Laser nanostructuring of thin films with ultrashort laser pulses is widely used for nanofabrication across various fields. A crucial parameter for optimizing and understanding the processes underlying laser processing is the absorbed laser fluence, which is essential for all damage phenomena such as melting, ablation, spallation, and delamination. While threshold fluences have been extensively studied for single compound thin films, advancements in ultrafast acoustics, magneto-acoustics, and acousto-magneto-plasmonics necessitate understanding the laser nanofabrication processes for functional multilayer films. In this work, we investigated the thickness dependence of ablation and delamination thresholds in Ni/Au bilayers by varying the thickness of the Ni layer. The results were compared with experimental data on Ni thin films. Additionally, we performed femtosecond time-resolved pump-probe measurements of transient reflectivity in Ni to determine the heat penetration depth and evaluate the melting threshold. Delamination thresholds for Ni films were found to exceed the surface melting threshold suggesting the thermal mechanism in a liquid phase. Damage thresholds for Ni/Au bilayers were found to be significantly lower than those for Ni and fingerprint the non-thermal mechanism without Ni melting, which we attribute to the much weaker mechanical adhesion at the Au/glass interface. This finding suggests the potential of femtosecond laser delamination for nondestructive, energy-efficient nanostructuring, enabling the creation of high-quality acoustic resonators and other functional nanostructures for applications in nanosciences. Full article
(This article belongs to the Section Nanophotonics Materials and Devices)
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<p>Optical microscopy of the structures obtained by a single fs-laser pulse on the Ni films in reflection. The upper set of photos demonstrates the structures for the different thicknesses of Ni film produced by the laser pulse coming from air at the same pulse energy (E<sub>p</sub> = 16 μJ). The lower set shows the same for the case of irradiation from the substrate side. The red quarter circles indicate the diameters of ablation craters, where the film was completely removed. The yellow quarter circle for air side ablation of 100 nm Ni indicates the ablation crater due to surface ablation. The scale, indicated for the 20 nm Ni ablation in air at 125 μm, applies to all other micrographs.</p>
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<p>Optical microscopy of the structures obtained by a single fs-laser pulse on the Ni/Au films in reflection. The upper set of photos demonstrates the structures for the different thicknesses of Ni/Au film produced by the laser pulse coming from air at a specified energy pulse (E<sub>p</sub> = 16 μJ). The lower panel shows the same for the case of irradiation from the substrate side. The red quarter circles indicate the diameters of ablation holes, where the film was completely removed (ablated). The thickness mentioned for NiAu refers to the thickness of the Ni layer deposited on a 5 nm Au layer, which is situated on the glass substrate. The scale, indicated for the 10 nm NiAu ablation in air at 125 μm, applies to all other micrographs.</p>
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<p>Optical microscopy of the structures obtained by a single fs-laser pulse on Ni and Ni/Au films on glass in reflection. The set of photos demonstrates the structures for the different thicknesses of Ni and Ni/Au film produced by the laser pulse coming from the glass side at specified energy pulses. The red quarter circles indicate the diameters of structures, obtained with delamination. The thickness mentioned for NiAu refers to the thickness of the Ni layer deposited on a 5 nm Au layer, which was situated on the glass substrate. The scale, indicated for the 80 nm Ni delamination at 50 μm, applies to all other micrographs.</p>
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<p>Surface displacement of Ni (<b>a</b>) and Ni/Au (<b>b</b>) delaminated films on both air and glass sides, as measured by interferometry.</p>
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<p>(<b>a</b>) Time-resolved reflectivity measurements of acoustic pulses in a Ni (240 nm)/sapphire sample, obtained by pumping at the nickel–air interface and probing at the nickel–sapphire interface, alongside the modeled reflectivity. (<b>b</b>) Acoustic spectrum derived from the experimental reflectivity data and the sensitivity function used for modeling the acoustic spectrum. (<b>c</b>) Simulated acoustic pulse and the sensitivity function employed in the modeling process. (<b>d</b>) Reconstructed strain obtained from experimental data and the corresponding modeled strain. The reflectivity data were well-approximated using a model strain with an exponential decay characterized by a heating depth <span class="html-italic">h</span> = 24 nm. Both the acoustic spectra and pulses were well-reproduced using the two-temperature (TTM) model by Saito et al. [<a href="#B44-nanomaterials-14-01488" class="html-bibr">44</a>]. The Fourier reconstructed strain was derived using the algorithm developed by Manke et al. [<a href="#B30-nanomaterials-14-01488" class="html-bibr">30</a>]. Time-resolved reflectivity measurements enable precise evaluation of the heating depth <span class="html-italic">h</span> up to the damage threshold.</p>
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<p>Ablation and delamination thresholds as a function of thickness for Ni (<b>a</b>) and Ni/Au (<b>b</b>) thin films, subjected to irradiation from both the air and substrate sides. The individual dots denote the thresholds evaluated using Liu’s method (for ease of visual interpretation, these dots are interconnected by lines). The black crossed point in (<b>a</b>) is a threshold value for incomplete Ni ablation. The green lines and the shaded area represent the calculated nickel/substrate interface melting threshold given by Equation (5) for <span class="html-italic">h</span> in a range from 20 nm to 30 nm. The purple lines/shaded area represent the calculated fluence required to heat the nickel at the Ni/Au interface to the melting temperature of gold (1377 K). Yellow squares represent the fs-laser-induced melting thresholds at the nickel–air surface, experimentally obtained by Wellershoff et al. [<a href="#B26-nanomaterials-14-01488" class="html-bibr">26</a>]. The thickness mentioned for NiAu refers to the thickness of the Ni layer deposited on a 5 nm Au layer, which is situated on the glass substrate.</p>
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17 pages, 15401 KiB  
Article
Investigation of Oxide Layer Development of X6CrNiNb18-10 Stainless Steel Exposed to High-Temperature Water
by Georg Veile, Radhika Hirpara, Simon Lackmann and Stefan Weihe
Materials 2024, 17(18), 4500; https://doi.org/10.3390/ma17184500 - 13 Sep 2024
Viewed by 236
Abstract
The oxide layer development of X6CrNiNb18-10 (AISI 347) during exposure to high-temperature water has been investigated. Stainless steels are known to form a dual oxide layer in corrosive environments. The secondary Fe-rich oxide layer has no significant protective effect. In contrast, the primary [...] Read more.
The oxide layer development of X6CrNiNb18-10 (AISI 347) during exposure to high-temperature water has been investigated. Stainless steels are known to form a dual oxide layer in corrosive environments. The secondary Fe-rich oxide layer has no significant protective effect. In contrast, the primary Cr-rich oxide layer is known to reach a stabilized state, protecting the base metal from further oxidation. This study’s purpose was to determine the development of oxide layer dimensions over exposure time using SEM, TEM and EDX line scans. While a parabolic development of Cr in the protective primary layer and Fe in the secondary layer was observed, the dimensions of the Ni layer remained constant. Ni required the presence of a pronounced Fe-rich secondary layer before being able to reside on the outer secondary layer. With increasing immersion time, the Ni element fraction surpassed the Cr element fraction in the secondary layer. Oxide growth on the secondary layer could be observed. After 480 h, nearly the entire surface was covered by the outer oxide layer. In the metal matrix, no depletion of Cr or Ni could be observed over time; however, an increased presence of Cr and Ni in the primary layer was found at the expense of Fe content. The Nb-stabilized stainless steel was subject to the formation of Niobium pentoxide (Nb2O5), with the quantity and magnitude of element fraction increasing over exposure time. Full article
(This article belongs to the Special Issue Corrosion and Formation of Surface Films on Metals and Alloys)
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<p>Schematic illustration of TEM EDX line scan results with two approaches to measure oxide layer thickness.</p>
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<p>SEM images of the oxidized surface after (<b>a</b>) 72 h, (<b>b</b>) 168 h and (<b>c</b>) 480 h exposure to HTW.</p>
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<p>Oxide film formed after 72 h in HTW with corresponding element maps of Fe, Cr, Nb, Ni and O, including the path of EDX line scans illustrated as a red arrow, performed by TEM.</p>
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<p>Results of corresponding EDX line scans of a specimen after being exposed to HTW for 72 h with reference to the markings in <a href="#materials-17-04500-f003" class="html-fig">Figure 3</a>.</p>
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<p>Oxide film formed after 168 h in HTW with corresponding element maps of Fe, Cr, Nb, Ni and O, including the path of EDX line scans illustrated as red arrows (performed by TEM).</p>
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<p>Results of corresponding EDX line scans of a specimen after being exposed to HTW for 168 h with reference to the markings in <a href="#materials-17-04500-f005" class="html-fig">Figure 5</a>.</p>
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<p>Oxide film formed after 480 h in HTW with corresponding element maps of Fe, Cr, Nb, Ni and O, including the path of EDX line scans illustrated with red arrows (performed by TEM).</p>
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<p>Results of corresponding EDX line scans of a specimen after being exposed to HTW for 480 h with reference to the markings in <a href="#materials-17-04500-f007" class="html-fig">Figure 7</a>.</p>
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<p>Element layer thickness of Cr, Ni and Fe over time in HTW with parabolic functions to replicate the oxide layer growth over exposure time, approximated with the least squares method.</p>
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<p>Maximum fraction of elements in inner layer measured with EDX line scans.</p>
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<p>XPS spectra of (<b>a</b>) Fe2p3/2, (<b>b</b>) Cr2p3/2, (<b>c</b>) Nb3d5/2 and (<b>d</b>) O1s after 20 days in HTW with the measured signal as black line and the accumulated approximation peaks as red line [<a href="#B29-materials-17-04500" class="html-bibr">29</a>].</p>
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12 pages, 3505 KiB  
Article
Preparation and Performance of Leather-Finished Plywood
by Yuanyuan Zou, Ziyi Yuan, Yuxin Lu, Xiaoqian Liu, Chuxuan Chen and Lu Fang
Polymers 2024, 16(18), 2587; https://doi.org/10.3390/polym16182587 - 13 Sep 2024
Viewed by 173
Abstract
In order to achieve batch production, we propose a simple and fast method to prepare leather-finished plywood. In this study, ethylene–vinyl acetate was selected as the intermediate layer to prepare EVA/polyurethane (PU) leather composites. ESEM, tensile property test and compressive property test were [...] Read more.
In order to achieve batch production, we propose a simple and fast method to prepare leather-finished plywood. In this study, ethylene–vinyl acetate was selected as the intermediate layer to prepare EVA/polyurethane (PU) leather composites. ESEM, tensile property test and compressive property test were used to characterize the microstructure and physical-mechanical properties of the composites. The response surface method (RSM) was also used to explore the relationship between hot pressing temperature, hot pressing pressure and hot pressing time. The significance of the factors and the interactions between the two factors were determined by ANOVA, with the most significant effect being that of the temperature. The theoretical optimal hot pressing process conditions were calculated by the regression equation as a temperature of 124.4 °C, a time of 200 s and a pressure of 1.3 MPa. The surface bond strength of the test specimen measured under this condition was 1.89 MPa, it has good finishing properties and the impregnation peel strength and surface bond strength met the requirements of GB/T 15104-2021. Full article
(This article belongs to the Special Issue New Challenges in Wood and Wood-Based Materials III)
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<p>Manufacturing process of PU-leather-finished plywood.</p>
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<p>Compression performance test of different materials: (<b>a</b>) deformation of PU leather, veneer and impregnated paper; (<b>b</b>) degree of deformation and compressing power of three materials; (<b>c</b>) microstructural changes in the PU leather during compression.</p>
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<p>Tensile performance test of different materials: (<b>a</b>) load–deformation curves of PU leather, veneer and impregnated paper; (<b>b</b>) tensile fracture energy and tensile strength of three materials; (<b>c</b>) microstructural changes in the PU leather during tensile and fracture tests and cross-sections of three materials.</p>
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<p>Effect of EVA on the tensile and compressive properties of leather: (<b>a</b>) tensile fracture energy and tensile strength of PU leather and EVA/PU leather composite materials; (<b>b</b>) degree of deformation and compressing power of PU leather and EVA/PU leather composite materials; (<b>c</b>) variation of deformation and load of two materials during tension; (<b>d</b>) variation of deformation and load of two materials during compression; (<b>e</b>) microstructural of leather before and after EVA lamination.</p>
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<p>Bonding interface microstructure of the decorative veneer: (<b>a</b>) 95 °C, 50 s, 1.0 MPa; (<b>b</b>) 125 °C, 150 s, 1.0 MPa; (<b>c</b>) 110 °C, 250 s, 1.5 MPa.</p>
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<p>The three-dimensional plots of the response surface: (<b>a</b>) the interaction between hot pressing temperature and time; (<b>b</b>) the interaction between hot pressing temperature and pressure; (<b>c</b>) the interaction between hot pressing time and pressure.</p>
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11 pages, 2739 KiB  
Article
Pressure-Promoted Triplet-Pair Separation in Singlet-Fission TIPS-Pentacene Nanofilms Revealed by Ultrafast Spectroscopy
by Lu Wang, Ruixue Zhu, Ruihua Pu, Weimin Liu, Yang Lu and Tsu-Chieu Weng
Nanomaterials 2024, 14(18), 1487; https://doi.org/10.3390/nano14181487 - 13 Sep 2024
Viewed by 215
Abstract
Singlet fission (SF), as an effective way to break through the Shockley–Queisser limit, can dramatically improve energy conversion efficiency in solar cell areas. The formation, separation, and relaxation of triplet-pair excitons directly affect the triplet yield, especially triplet-pair separation; thus, how to enhance [...] Read more.
Singlet fission (SF), as an effective way to break through the Shockley–Queisser limit, can dramatically improve energy conversion efficiency in solar cell areas. The formation, separation, and relaxation of triplet-pair excitons directly affect the triplet yield, especially triplet-pair separation; thus, how to enhance the triplet-pair separation rate becomes one of the key points to improve SF efficiency; the decay mechanism where the singlet state is converted into two triplet states is significant for the study of the SF mechanism. Herein, we employ ultrafast transient absorption spectroscopy to study the singlet-fission process of nano-amorphous 6, 13-bis(triisopropylsilylethynyl)-Pentacene (TIPS-pentacene) films in a diamond anvil cell (DAC). A kinetics model related to the structural geometric details, as well as an evaluation of the pressure manipulation impacts, is demonstrated based on the experimental results. The results indicate that pressure manipulation enhanced the triplet-pair separation rates of SF-based materials according to their structural micro-environmental improvement when compressed in DAC, while the triplet-exciton transportation lifetime is prolonged. This work shows that pressure may effectively optimize the structural disorder of SF materials, which were found to improve triplet-pair separation efficiency and potentially offer an effective way to further improve SF efficiency. Full article
(This article belongs to the Special Issue Two-Dimensional Semiconductor Nanostructure and Nanomaterials)
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<p>The chemical formula of TPN and the nano-amorphous thin film with sapphire as substrate.</p>
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<p>The structure diagram of the Diamond Anvil Cell.</p>
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<p>Pressure-dependent steady-state absorption spectra of amorphous TPN film.</p>
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<p>(<b>a</b>,<b>b</b>) Femtosecond transient absorption spectra of TPN amorphous film under atmospheric pressure with 515 nm excitation. (<b>c</b>,<b>d</b>) Comparison of the fs-transient absorption spectra of TPN amorphous film under various pressures. Normalizing the characteristic peaks at free triplets and the pairs of bound triplets, it can be observed that the characteristic peaks of both free-triplet and bound-triplet pairs move toward the long wave with the increase in pressure.</p>
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<p>Comparison of the fs-transient absorption spectra of TPN amorphous film under (<b>a</b>) 0 GPa, (<b>b</b>) 0.73 GPa, (<b>c</b>) 1.71 GPa, and (<b>d</b>) 3.64 GPa pressures, which shows that the proportion of free triplets and bound triplets changes with the increase in pressure.</p>
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<p>Diagram of singlet-fission process facilitated by different pressures. Pressure under 0.73 GPa promotes singlet fission into triplet pairs, then pressure between 0.73 GPa and 3.64 GPa promotes triplet pairs into free triplets.</p>
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<p>The schematic diagram of the effect of pressurization on the promotion of singlet fission in amorphous TPN films.</p>
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<p>Comparison of the dynamics of TPN amorphous film under various pressures: (<b>a</b>) The kinetics of free triplets at 560 nm, and (<b>b</b>) the kinetics of triplet pairs at 900 nm. The points in the figure represent the collected experimental data points, while the curve represents the data fitting of the constructed model.</p>
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9 pages, 2948 KiB  
Article
Ultraviolet Light-Induced Surface Changes of Tungsten Oxide in Air: Combined Scanning Transmission Electron Microscopy and X-ray Photoelectron Spectroscopy Analysis
by Yuki Nakagawa, Yasuhiro Shiratsuchi, Tamaki Shibayama and Masaki Takeguchi
Nanomaterials 2024, 14(18), 1486; https://doi.org/10.3390/nano14181486 - 13 Sep 2024
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Abstract
Scanning transmission electron microscopy (STEM) and X-ray photoelectron spectroscopy analyses were combined to clarify the ultraviolet light-induced surface changes of WO3 in air. Identical-location STEM (IL-STEM) analysis showed that the WO3 particle surface was covered with an amorphous thin film after [...] Read more.
Scanning transmission electron microscopy (STEM) and X-ray photoelectron spectroscopy analyses were combined to clarify the ultraviolet light-induced surface changes of WO3 in air. Identical-location STEM (IL-STEM) analysis showed that the WO3 particle surface was covered with an amorphous thin film after ultraviolet irradiation in air. X-ray photoelectron spectroscopy analysis showed that hydrocarbon decomposition and the formation of carboxyl/hydroxyl species occurred. These results suggested that the amorphous thin films consisted of photocatalytic oxidative species of hydrocarbon. The IL-STEM analysis could detect small light-induced changes. This technique will be useful for the microscopic characterization of photocatalysis or photoinduced hydrophilic conversion. Full article
(This article belongs to the Special Issue Nanoscale Microscopy Techniques for Energy Materials)
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<p>(<b>a</b>,<b>b</b>) HAADF-STEM images of WO<sub>3</sub> powders: (<b>a</b>) pristine WO<sub>3</sub>, and (<b>b</b>) after 4 h of UV irradiation. (<b>c</b>) XRD profile the WO<sub>3</sub> powder, plates (A-1, A-2, and B-2), and reference pattern of monoclinic WO<sub>3</sub>.</p>
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<p>(<b>a</b>) High-magnification HAADF-STEM image of pristine WO<sub>3</sub> particles. (<b>b</b>) Atomic structure model of monoclinic WO<sub>3</sub> along the [001] zone axis. Gray atoms and red atoms represent W and O, respectively. (<b>c</b>–<b>h</b>) Atomic-scale HAADF-STEM images of WO<sub>3</sub> particles before and after UV irradiation.</p>
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<p>(<b>a</b>) Photographs of the A-1 and B-1 plates. (<b>b</b>) C 1s XPS spectra of the A-1 and A-2 plates. (<b>c</b>) C 1s XPS spectra of the B-1 and B-2 plates. (<b>d</b>) Normalized C 1s XPS spectra of all the plates. Explanation of each color line was same for that of <a href="#nanomaterials-14-01486-f003" class="html-fig">Figure 3</a>e. (<b>e</b>) Normalized O 1s XPS spectra of all the plates. (<b>f</b>) Normalized W 4f XPS spectra of all the plates. Explanation of each color line was same for that of <a href="#nanomaterials-14-01486-f003" class="html-fig">Figure 3</a>e. (<b>g</b>) C 1s spectra of the B-2 plate deconvoluted into three peaks. (<b>h</b>) O 1s spectra of the B-2 plate deconvoluted into three peaks.</p>
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12 pages, 4198 KiB  
Article
Decorating TiO2 Nanoparticle Thin Film with SnSx (x < 1): Preparation, Characterization, and Photocatalytic Activity
by Fang Xu, Nicola Scaramuzza and Carlo Versace
Coatings 2024, 14(9), 1185; https://doi.org/10.3390/coatings14091185 - 12 Sep 2024
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Abstract
We report a study on the SnSx (x < 1) decoration of porous TiO2 nanoparticle thin films using the ionic layer adsorption and reaction (ILAR) method. UV-vis absorption measurements revealed a direct bandgap of 1.40–2.10 eV for SnSx (with [...] Read more.
We report a study on the SnSx (x < 1) decoration of porous TiO2 nanoparticle thin films using the ionic layer adsorption and reaction (ILAR) method. UV-vis absorption measurements revealed a direct bandgap of 1.40–2.10 eV for SnSx (with x = 0.85) and 3.15 eV for TiO2. Degradation of rhodamine B molecules in aqueous solutions shows that coating with a Sn-to-Ti molar ratio of 2% improves the efficiency of the photocatalytic performance of titanium dioxide, but excessive coverage decreases it. We interpret the observed behavior as due to a delicate balance of many competing factors. The formation of intimate interfaces guaranteed by the ILAR growth technique and a nearly optimal alignment of conduction band edges facilitate electron transfer, reducing electron–hole recombination rates. However, the valence hole transfer from TiO2 to SnS reduces the oxidative potential, which is crucial in the degradation mechanism. Full article
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<p>SEM images of a pure TiO<sub>2</sub> thin film (<b>A</b>,<b>C</b>) and an SnS<span class="html-italic"><sub>x</sub></span> (Sn100S600)-coated TiO<sub>2</sub> film (<b>B</b>,<b>D</b>). The beam energy was 5 keV for (<b>A</b>,<b>B</b>) and 10 keV for (<b>C</b>,<b>D</b>), while the magnification was 500 k for all images.</p>
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<p>Cross-sectional SEM image showing a TiO<sub>2</sub> thin film about 11 μm thick.</p>
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<p>EDX spectra for a pure TiO<sub>2</sub> thin film (<b>A</b>) and two SnS<span class="html-italic"><sub>x</sub></span>-coated TiO<sub>2</sub> thin films (<b>B</b>,<b>C</b>). Also indicated are the molar ratios between various elements.</p>
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<p>XRD pattern for a pure TiO<sub>2</sub> nanoparticle (P25) thin film deposited on an FTO-grazed glass substrate (a); decorated with SnS<span class="html-italic"><sub>x</sub></span> Sn020S120 (b); Sn100S600 (c); and Sn100S600 (5 cycles) (d).</p>
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<p>XPS spectra of Ti 2p, O 1s, Sn 3d, and S 2p levels for films of pure TiO<sub>2</sub> (Sn000S000) and SnS<span class="html-italic"><sub>x</sub></span>-coated (Sn100S600) TiO<sub>2</sub> films.</p>
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<p>Upper panel: UV-vis optical absorption spectra of pure TiO<sub>2</sub> thin film and decorated TiO<sub>2</sub> films with SnS<span class="html-italic"><sub>x</sub></span> NPs of different amounts; Lower panel: bandgap energy determination made using the Tauc plots.</p>
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<p>Upper panel: Time evolution of the RhB absorption spectra for the sample Sn005S030. Middle panel: Relative RhB concentration change C(t)/C<sub>0</sub> as a function of Xe lamp irradiation time t for various SnS<span class="html-italic"><sub>x</sub></span>@TiO<sub>2</sub> films. The lines are the linear fittings. Lower panel: The zero-order degradation rate constant vs. Sn-to-Ti molar ratio.</p>
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<p>Energy level potential diagram of SnS, TiO<sub>2</sub>, RhB, and relevant redox reactions.</p>
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