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11 pages, 1731 KiB  
Article
Highly Stable Flexible Organic Electrochemical Transistors with Natural Rubber Latex Additives
by Miguel Henrique Boratto, Carlos F. O. Graeff and Sanggil Han
Polymers 2024, 16(16), 2287; https://doi.org/10.3390/polym16162287 (registering DOI) - 13 Aug 2024
Abstract
Organic electrochemical transistors (OECTs) have attracted considerable interest in the context of wearable and implantable biosensors due to their remarkable signal amplification combined with seamless integration into biological systems. These properties underlie OECTs’ potential utility across a range of bioelectronic applications. One of [...] Read more.
Organic electrochemical transistors (OECTs) have attracted considerable interest in the context of wearable and implantable biosensors due to their remarkable signal amplification combined with seamless integration into biological systems. These properties underlie OECTs’ potential utility across a range of bioelectronic applications. One of the main challenges to their practical applications is the mechanical limitation of PEDOT:PSS, the most typical conductive polymer used as a channel layer, when the OECTs are applied to implantable and stretchable bioelectronics. In this work, we address this critical issue by employing natural rubber latex (NRL) as an additive in PEDOT:PSS to improve flexibility and stretchability of the OECT channels. Although the inclusion of NRL leads to a decrease in transconductance, mainly due to a reduced carrier mobility from 0.3 to 0.1 cm2/V·s, the OECTs maintain satisfactory transconductance, exceeding 5 mS. Furthermore, it is demonstrated that the OECTs exhibit excellent mechanical stability while maintaining their performance even after 100 repetitive bending cycles. This work, therefore, suggests that the NRL/PEDOT:PSS composite film can be deployed for wearable/implantable applications, where high mechanical stability is needed. This finding opens up new avenues for practical use of OECTs in more robust and versatile wearable and implantable biosensors. Full article
(This article belongs to the Special Issue Flexible Electronics Applications of Polymer Materials)
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Figure 1

Figure 1
<p>Schematics of (<b>a</b>) latex/PEDOT:PSS film preparation and (<b>b</b>) an OECT structure.</p>
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<p>(<b>a</b>) Optical microscope images of the OECT channels (10× magnification). Geometry of the channels: W/L = 9.5. (<b>b</b>) Transfer and (<b>c</b>) transconductance curves of the flexible OECTs. (<b>d</b>) Carrier mobility and (<b>e</b>) channel capacitance of all samples. All the measurements were performed by an Ag/AgCl gate at <span class="html-italic">V</span><sub>D</sub> = −0.8 V, and in (<b>d</b>,<b>e</b>), the data were obtained by applying AC modulation at the gate electrode.</p>
Full article ">Figure 3
<p>(<b>a</b>) Schematic of the repetitive bending test of the flexible OECTs. (<b>b</b>) Transconductance curves of all samples at <span class="html-italic">V</span><sub>D</sub> = −0.8 V before and after bending stress. Output curves of (<b>c</b>) PEDOT:PSS and (<b>d</b>) 8% NRL/PEDOT:PSS before and after bending stress. <span class="html-italic">V</span><sub>G</sub> step of +0.2 V.</p>
Full article ">Figure 4
<p>(<b>a</b>) Current degradation (<span class="html-italic">I</span>/<span class="html-italic">I</span><sub>0</sub>) as a function of elongation percentage. (<b>b</b>) Real-time current response when the 6% NRL/PEDOT:PSS thin film was elongated up to 70% and then returned to its original size. (<b>c</b>) Microscope images of samples (i) before and (ii) after stretching. Samples: PEDOT:PSS and 6% NRL/PEDOT:PSS thin films spin-coated on latex substrates.</p>
Full article ">
14 pages, 3250 KiB  
Article
Three-Layered Composite Scintillator Based on the Epitaxial Structures of YAG and LuAG Garnets Doped with Ce3+ and Sc3+ Impurities
by Sandra Witkiewicz-Łukaszek, Vitalii Gorbenko, Tetiana Zorenko, Jan Pejchal, Jiri A. Mares, Romana Kucerkova, Alena Beitlerova, Martin Nikl, Oleg Sidletskiy, Janusz Winiecki, Carmelo D’Ambrosio and Yuriy Zorenko
Materials 2024, 17(16), 4025; https://doi.org/10.3390/ma17164025 (registering DOI) - 13 Aug 2024
Abstract
In this study, we propose novel three-layer composite scintillators designed for the simultaneous detection of different ionizing radiation components. These scintillators are based on epitaxial structures of LuAG and YAG garnets, doped with Ce3+ and Sc3+ ions. Samples of these composite [...] Read more.
In this study, we propose novel three-layer composite scintillators designed for the simultaneous detection of different ionizing radiation components. These scintillators are based on epitaxial structures of LuAG and YAG garnets, doped with Ce3+ and Sc3+ ions. Samples of these composite scintillators, containing YAG:Ce and LuAG:Ce single crystalline films with different thicknesses and LuAG:Sc single crystal substrates, were grown using the liquid phase epitaxy method from melt solutions based on PbO-B2O3 fluxes. The scintillation properties of the proposed composites, YAG:Ce film/LuAG:Sc film/LuAG:Ce crystal and YAG:Ce film/LuAG:Ce film/LuAG:Sc crystal, were investigated under excitation by radiation with α-particles from a 239Pu source, β-particles from 90Sr sources and γ-rays from a 137Cs source. Considering the properties of the mentioned composite scintillators, special attention was paid to the ability of simultaneous separation of the different components of mixed ionizing radiation containing the mentioned particles and quanta using scintillation decay kinetics. The differences in scintillation decay curves under α- and β-particle and γ-ray excitations were characterized using figure of merit (FOM) values at various scintillation decay intensity levels (1/e, 0.1, 0.05, 0.01). Full article
(This article belongs to the Section Optical and Photonic Materials)
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Figure 1

Figure 1
<p><b>Left</b>—scheme of three-layered composite scintillator for simultaneous registration of α- and β-particles and γ-rays. <b>Right</b>—three-layered composite scintillators YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC (<b>left</b>) and YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC (<b>right</b>).</p>
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<p>(<b>a</b>) Scheme of three-layered composite scintillator for simultaneous registration of α- and β-particles and γ-rays. (<b>b</b>) Three-layered composite scintillators YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC (<b>a</b>) and YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC (<b>b</b>).</p>
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<p>Normalized CL (<b>a</b>) and RL (<b>b</b>) spectra of YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC and YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC.</p>
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<p>PHS of LuAG:Ce SC substrate (1) and two-layered LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC structure (2), as well as three-layered YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC composite scintillators (3), were measured with a shaping time of 3 µs. Measurements were conducted under α-particle excitation with an energy of 5.4857 MeV by a <sup>241</sup>Am source (<b>a</b>) and under γ-ray excitation with an energy of 662 keV by a <sup>137</sup>Cs source (<b>b</b>).</p>
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<p>PHS of LuAG:Sc SC substrate (1), two-layered LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC structure (2) and three-layered YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC (3) composite scintillators were measured in a time range of 3 µs. Measurements were conducted under α-particle excitation with an energy of 5.4857 MeV by a <sup>241</sup>Am source (<b>a</b>) and under γ-ray excitation from a <sup>137</sup>Cs source with an energy of 662 keV (<b>b</b>).</p>
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<p>PHS of YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC composite scintillators measured with shaping time in the 0.5–10 µs range under α-particle excitation with an energy of 5.15 MeV from a <sup>239</sup>Pu source (<b>a</b>) and under γ-ray excitation from a <sup>137</sup>Cs source with an energy of 662 keV (<b>b</b>).</p>
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<p>PHS of YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC composite scintillators measured with shaping time in the 0.5–10 µs range under α-particle excitation with an energy of 5.15 MeV from a <sup>239</sup>Pu source (<b>a</b>) and under γ-ray excitation from a <sup>137</sup>Cs source with an energy of 662 keV (<b>b</b>).</p>
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<p>Dependence of the LY of the YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Sc SC (1) and YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC (2) composite scintillators under excitation by α-particles from a <sup>239</sup>Pu source (<b>a</b>) and γ-rays from a <sup>137</sup>Cs source (<b>b</b>).</p>
Full article ">Figure 9
<p>(<b>a</b>) Scintillation decay curves of YAG:Ce SCF<sub>2</sub>/LuAG:Sc SCF<sub>1</sub>/LuAG:Ce SC composite scintillators under excitation by α- and β-particles and γ-quanta. (<b>b</b>) FOM values under registration of the mentioned types of radiation.</p>
Full article ">Figure 10
<p>(<b>a</b>) Separation of the scintillation decay curves of YAG:Ce SCF<sub>2</sub>/LuAG:Ce SCF<sub>1</sub>/LuAG:Sc SC composite scintillators under excitation by α- and β-particles and γ-quanta. (<b>b</b>) FOM values of the mentioned composite scintillators under registration of the mentioned types of radiation.</p>
Full article ">
17 pages, 4121 KiB  
Article
Plasma-Enhanced Atomic Layer Deposition of Hematite for Photoelectrochemical Water Splitting Applications
by Thom R. Harris-Lee, Andrew Brookes, Jie Zhang, Cameron L. Bentley, Frank Marken and Andrew L. Johnson
Crystals 2024, 14(8), 723; https://doi.org/10.3390/cryst14080723 (registering DOI) - 13 Aug 2024
Abstract
Hematite (α-Fe2O3) is one of the most promising and widely used semiconductors for application in photoelectrochemical (PEC) water splitting, owing to its moderate bandgap in the visible spectrum and earth abundance. However, α-Fe2O3 is limited by [...] Read more.
Hematite (α-Fe2O3) is one of the most promising and widely used semiconductors for application in photoelectrochemical (PEC) water splitting, owing to its moderate bandgap in the visible spectrum and earth abundance. However, α-Fe2O3 is limited by short hole-diffusion lengths. Ultrathin α-Fe2O3 films are often used to limit the distance required for hole transport, therefore mitigating the impact of this property. The development of highly controllable and scalable ultrathin film deposition techniques is therefore crucial to the application of α-Fe2O3. Here, a plasma-enhanced atomic layer deposition (PEALD) process for the deposition of homogenous, conformal, and thickness-controlled α-Fe2O3 thin films (<100 nm) is developed. A readily available iron precursor, dimethyl(aminomethyl)ferrocene, was used in tandem with an O2 plasma co-reactant at relatively low reactor temperatures, ranging from 200 to 300 °C. Optimisation of deposition protocols was performed using the thin film growth per cycle and the duration of each cycle as optimisation metrics. Linear growth rates (constant growth per cycle) were measured for the optimised protocol, even at high cycle counts (up to 1200), confirming that all deposition is ‘true’ atomic layer deposition (ALD). Photoelectrochemical water splitting performance was measured under solar simulated irradiation for pristine α-Fe2O3 deposited onto FTO, and with a α-Fe2O3-coated TiO2 nanorod photoanode. Full article
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Figure 1

Figure 1
<p>Thermogravimetric analysis of DMAMFc, measured under an Ar flow between 30 and 520 °C at a constant ramp rate of 5 °C min<sup>−1</sup>, with volatilisation onset marked with a red dashed line.</p>
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<p>Optimisation of DMAMFc PEALD pulse sequence process, comparing measured growth rate to (<b>a</b>) DMAMFc delivery boost pulse, and (<b>b</b>) DMAMFc delivery pulse for a single boost pulse before plasma step (blue, zoomed on inset), and multiple boost pulse sequences before the plasma step (black). All depositions completed with the defined ‘standard protocol’ except for the single varied parameter.</p>
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<p>Optimisation of DMAMFc PEALD temperatures, comparing measured growth rate with (<b>a</b>) pot temperature, and (<b>b</b>) chamber temperature. All depositions completed with the defined ‘standard protocol’ except for the single varied parameter.</p>
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<p>Optimisation of DMAMFc PEALD plasma parameters, comparing measured growth rate with (<b>a</b>) plasma power, and (<b>b</b>) plasma pulse length. All depositions completed with the defined ‘standard protocol’ except for the single varied parameter. (<b>c</b>) Comparison of pulse/purge/pulse/purge protocols for pulsed vs. flow plasma gas input, and (<b>d</b>) measured growth from pulsed vs. flow plasma gas protocols, with and without RF pulse.</p>
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<p>Growth rates and corresponding deposition efficiencies (<span class="html-italic">η</span>) for a series of PEALD processes.</p>
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<p>Growth rate and total film thickness measurements for films deposited by PEALD using process 6 across a range of total cycle numbers.</p>
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<p>Appearance (from left to right) of: initial FTO-coated glass substrate, as-deposited 60 nm thin films, annealed 60 nm thin film (note that the silver area at the top is silver paint and not part of the sample).</p>
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<p>Grazing incidence X-ray diffraction patterns for pristine FTO (red), (blue) as-deposited Fe<sub>2</sub>O<sub>3</sub> on FTO, and annealed Fe<sub>2</sub>O<sub>3</sub> on FTO (black), measured at an X-ray incidence angle of 5° for ~12 h within a 2θ range of (<b>a</b>) 20–90° and (<b>b</b>) 30–40°. Insets show zoomed views of the peak of interest with XRD patterns overlayed. Peaks associated with FTO are marked with a black dot.</p>
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<p>(<b>a</b>) FE-SEM cross-section image of 60 nm-α-Fe<sub>2</sub>O<sub>3</sub> deposited onto FTO-coated glass substrate (approximate α-Fe<sub>2</sub>O<sub>3</sub> layer indicated in red). EDX data for 60 nm-α-Fe<sub>2</sub>O<sub>3</sub> deposited onto FTO-coated glass substrate: (<b>b</b>) electron image overlayed with Fe series from EDX analysis (teal), (<b>c</b>) Fe map across electron image, and (<b>d</b>) Sn map across the electron image.</p>
Full article ">Figure 10
<p>FE-SEM surface images of (<b>a</b>) TiO<sub>2</sub>-nanorods, and (<b>b</b>) TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60nm, deposited onto FTO-coated glass substrate.</p>
Full article ">Figure 11
<p>(<b>a</b>) FE-SEM cross-section image of TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-30 nm, (<b>b</b>) electron image of TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-30 nm overlayed with Fe (blue) and Ti (orange) series from EDX analysis, (<b>c</b>) FE-SEM cross-section image of TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60 nm, and (<b>d</b>) electron image of TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60 nm overlayed with Fe (blue) and Ti (orange) series from EDX analysis.</p>
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<p>(<b>a</b>) Optical absorption spectra for: (black) TiO<sub>2</sub>, (red) α-Fe<sub>2</sub>O<sub>3</sub>, (blue) TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>. (<b>b</b>) Tauc plots for each sample with extrapolated indirect bandgaps as annotated. All thin films were deposited onto FTO-coated glass.</p>
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<p>X-ray diffraction pattern for the pristine TiO<sub>2</sub> nanorod and TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60 nm samples, both grown onto FTO-coated glass substrate. Peak locations corresponding to rutile TiO<sub>2</sub> and a-Fe<sub>2</sub>O<sub>3</sub> are highlighted in blue and red, respectively, and FTO is marked with a black dot.</p>
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<p>Linear sweep voltammograms under one sun-chopped AM 1.5 (<b>a</b>,<b>c</b>) front, (<b>b</b>,<b>d</b>) rear illumination for (black) TiO<sub>2</sub>, (red) 30 nm α-Fe<sub>2</sub>O<sub>3</sub>, ((<b>a</b>,<b>b</b>); blue) TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-30nm, ((<b>c</b>,<b>d</b>); blue TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60 nm). Insets contain zoomed-in views ignoring the cathodic current density baseline shift. All measurements performed in 1 M KOH (pH 13.7) with a 15 mV s<sup>−1</sup> scan rate.</p>
Full article ">Figure 15
<p>Incident photon-electron conversion efficiencies measured at 1.23 V vs. RHE under one sun AM 1.5 rear illumination for (i) as-deposited TiO<sub>2</sub>, and (ii) TiO<sub>2</sub>/Fe<sub>2</sub>O<sub>3</sub>-60 nm. All measurements carried out 1 M KOH (pH 13.7).</p>
Full article ">
32 pages, 9337 KiB  
Review
Benefits of Incorporating Lignin into Starch-Based Films: A Brief Review
by Lamia Zuniga Linan, Farayde Matta Fakhouri, Gislaine Ferreira Nogueira, Justin Zoppe and José Ignacio Velasco
Polymers 2024, 16(16), 2285; https://doi.org/10.3390/polym16162285 - 13 Aug 2024
Abstract
Polysaccharides are an excellent renewable source for developing food-packing materials. It is expected that these packages can be an efficient barrier against oxygen; can reduce lipid peroxidation, and can retain the natural aroma of a food commodity. Starch has tremendous potential to be [...] Read more.
Polysaccharides are an excellent renewable source for developing food-packing materials. It is expected that these packages can be an efficient barrier against oxygen; can reduce lipid peroxidation, and can retain the natural aroma of a food commodity. Starch has tremendous potential to be explored in the preparation of food packaging; however, due to their high hydrophilic nature, packaging films produced from starch possess poor protective moisture barriers and low mechanical properties. This scenario limits their applications, especially in humid conditions. In contrast, lignin’s highly complex aromatic hetero-polymer network of phenylpropane units is known to play a filler role in polysaccharide films. Moreover, lignin can limit the biodegradability of polysaccharides films by a physical barrier, mainly, and by non-productive bindings. The main interactions affecting lignin non-productive bindings are hydrophobic interactions, electrostatic interactions, and hydrogen-bonding interactions, which are dependent on the total phenolic –OH and –COOH content in its chemical structure. In this review, the use of lignin as a reinforcement to improve the biodegradability of starch-based films in wet environments is presented. Moreover, the characteristics of the used lignins, the mechanisms of molecular interaction among these materials, and the sensitive physicochemical parameters for biodegradability detection are related. Full article
(This article belongs to the Collection Lignin)
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Figure 1
<p>Distribution of lignin in wood cell walls. Adapted with permission from Sjöström, 1993 [<a href="#B30-polymers-16-02285" class="html-bibr">30</a>], copyright 30 July 2024 Elsevier license No 5838970067490.</p>
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<p>Lignin classification according to the precursor. Font: (<b>a</b>) <a href="https://www.infoholicresearch.com/report/kraft-lignin-market/" target="_blank">https://www.infoholicresearch.com/report/kraft-lignin-market/</a>, accessed on 30 July 2024; (<b>b</b>) Zuniga Linan et al. [<a href="#B32-polymers-16-02285" class="html-bibr">32</a>]; (<b>c</b>) <a href="https://tree-pictures.com/images/treephotos-poplar/poplartree/poplar-tree-bark.jpg" target="_blank">https://tree-pictures.com/images/treephotos-poplar/poplartree/poplar-tree-bark.jpg</a>, accessed on 30 July 2024; (<b>d</b>) The authors; (<b>e</b>) <a href="https://stock.adobe.com/es/search?k=%22rice%20husk%22" target="_blank">https://stock.adobe.com/es/search?k=%22rice%20husk%22</a>, accessed on 30 July 2024; (<b>f</b>) <a href="https://pt.dreamstime.com/foto-de-stock-casca-seca-do-coco-image67395503" target="_blank">https://pt.dreamstime.com/foto-de-stock-casca-seca-do-coco-image67395503</a>, accessed on 30 July 2024; (<b>g</b>) Font: <a href="https://www.revistarural.com.br/2020/06/02/pesquisa-permite-gerar-etanol-a-partir-de-bagaco-de-cana/" target="_blank">https://www.revistarural.com.br/2020/06/02/pesquisa-permite-gerar-etanol-a-partir-de-bagaco-de-cana/</a>, accessed on 30 July 2024; (<b>h</b>) Font: <a href="https://pt.dreamstime.com/fundo-da-palha-do-arroz-image108812076" target="_blank">https://pt.dreamstime.com/fundo-da-palha-do-arroz-image108812076</a>, accessed on 30 July 2024.</p>
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<p>“Core-shell” structure of a lignin nanoparticle (<b>a</b>) and the cluster aggregation of LNP spheres (<b>b</b>). Adapted with permission from SHUZHEN NI, HUIYANG BIAN, YONGCHAO ZHANG, et al., 2022 [<a href="#B37-polymers-16-02285" class="html-bibr">37</a>]. Copyright, 7 July 2024 American Chemical Society).</p>
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<p>Flow diagram of preparation of LNPs from the black liquor extracted with the p-TsOH method. Reused with permission from Ma et al., 2018 [<a href="#B48-polymers-16-02285" class="html-bibr">48</a>]. Copyright 08 August 2024 DE GRUYTER.</p>
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<p>Structures of most abundant linkages in lignin.</p>
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<p>Multiscale structural representation of the HGS lignin built through LigninGraphs software. (<b>a</b>) C-O bond representation; (<b>b</b>) H monomer; (<b>c</b>) lignin polymer of 12 monomers; (<b>d</b>) big graph for the lignin polymer, where each monomer is a node, and each linkage is an edge. The large repeat units are represented in colorful hexagons, blue (S-unit), green (G-unit), and red (H-unit). Adapted with permission from Wang et al., 2022 [<a href="#B52-polymers-16-02285" class="html-bibr">52</a>]. Copyright, 24 July 2024 Springer Nature.</p>
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<p>The slow-release fertilizer’s biodegradability due to urea-crosslinked starch films is influenced by the lignin macromolecule. Lignin macromolecule’s implication in slowing the biodegradability of urea-crosslinked starch films applied as slow-release fertilizer. Reprinted with permission from Majeed et al., 2017 [<a href="#B70-polymers-16-02285" class="html-bibr">70</a>]. Copyright, 24 July 2024 John Wiley and Sons, License No. 5835691379483.</p>
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<p>Effect of the LNPs from DES, organosolv, and soda lignins on the WHC of bacterial cellulose composite films. The figure was built with experimental data by Tian et al., 2021 [<a href="#B62-polymers-16-02285" class="html-bibr">62</a>]. Copyright, 24 July 2024 Elsevier license No 5835701089403.</p>
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<p>Effect of alkali lignin on the WVP permeability of sago-starch/alkali lignin films. Reprinted with permission from Bhat et al., 2013 [<a href="#B67-polymers-16-02285" class="html-bibr">67</a>]. Copyright, 30 July 2024 Elsevier No. 5838970804070.</p>
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<p>Effect of 20% LNPs in the CA of water, diiodomethane (Dio), and glycerol (Gly) on starch film. Reprinted with permission from Roostazadesh et al., 2022 [<a href="#B92-polymers-16-02285" class="html-bibr">92</a>]. Copyright, 30 July 2024 Elsevier No. 5838601217527.</p>
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<p>Effect of LNPs in the DCA of LNPs/starch films intended to be used as packaging materials. Adapted with permission from Ni et al., 2022 [<a href="#B37-polymers-16-02285" class="html-bibr">37</a>]. Copyright, 30 July 2024 American Chemical Society.</p>
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<p>Soy protein isolate films with several concentrations of lignosulfonate and alkali lignin (2, 4, 6, and 10 g of lignin/100 g of soy protein). Adapted with permission from Zadeh, O’Keefe, and Kim, 2018 [<a href="#B40-polymers-16-02285" class="html-bibr">40</a>]. Copyright, CC-BY license, 30 July 2024 ACS Publications.</p>
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<p>Impact of lignin content and presence on the starch/lignin films’ mechanical performance. Reprinted with permission from Roostazadesh et al., 2022 [<a href="#B92-polymers-16-02285" class="html-bibr">92</a>]. Copyright, 30 July 2024 Elsevier No. 5838601217527.</p>
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<p>Impact of lignin on the starch/lignin films’ thermal characteristics. (<b>a</b>) TPSL0, (<b>b</b>) TPSL1.2, (<b>c</b>) TPSL1.6, (<b>d</b>) TPSL2.0, (<b>e</b>) TPSL2.4). (Reprinted with permission from Çalgeris et al., 2012 [<a href="#B94-polymers-16-02285" class="html-bibr">94</a>]. Copyright, 30 July 2024 John Wiley and Sons, License No. 583861050189).</p>
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<p>Flow curves of HDPE and HDPE/lignin blends. Reprinted with permission from Sameni, Jaffer, and Sain, 2018 [<a href="#B93-polymers-16-02285" class="html-bibr">93</a>]. Copyright, 30 July 2024 Elsevier No. 5838980606723.</p>
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<p>FTIR spectrum of lignin-reinforced films, pristine and biodegraded in aerobic soil. (Reprinted with permission from Majeed et al., 2017 [<a href="#B70-polymers-16-02285" class="html-bibr">70</a>]. Copyright, 24 July 2024 John Wiley and Sons, License No. 5835691379483.</p>
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<p>SEM images of surface (<b>a</b>,<b>b</b>) of the pure starch film and starch-1% LNPs film, respectively; (<b>c</b>) cross section of the starch-1% LNPs film with microclusters; (<b>d</b>) illustration of the distribution of LPNs in the starch film and the formed possible rough structure. Adapted with permission from Ni et al., 2022 [<a href="#B37-polymers-16-02285" class="html-bibr">37</a>]. Copyright, 30 July 2024 American Chemical Society.</p>
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<p>Improvement of the crystallinity of starch-lignin films with the addition of up to 20 wt% of soda lignin. (Reprinted with permission from Roostazadesh et al., 2022 [<a href="#B92-polymers-16-02285" class="html-bibr">92</a>]. Copyright, 16 June 2023 Elsevier No. 5570960318321).</p>
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11 pages, 4145 KiB  
Article
Asphalt-Binder Mixtures Evaluated by T1 NMR Relaxometry
by Rebecca M. Herndon, Jay Balasubramanian, Magdy Abdelrahman and Klaus Woelk
Physchem 2024, 4(3), 285-295; https://doi.org/10.3390/physchem4030020 (registering DOI) - 13 Aug 2024
Abstract
Asphalt pavements make up a majority of the essential transportation systems in the US. Asphalt mixtures age and degrade over time, reducing the pavement performance. Pavement performance critically depends on the aging of asphalt binder. The aging of asphalt binder during construction is [...] Read more.
Asphalt pavements make up a majority of the essential transportation systems in the US. Asphalt mixtures age and degrade over time, reducing the pavement performance. Pavement performance critically depends on the aging of asphalt binder. The aging of asphalt binder during construction is traditionally modeled by rolling thin film oven (RTFO) testing, while aging during service life is modeled by pressure aging vessel (PAV) testing. Comparing these models to the aging of binders in actual pavements is limited because, to be used for current testing, binders must be separated from the pavement’s aggregate by solvent extraction. Solvent extraction will, at least in part, compromise the structural integrity of asphalt binder samples. Spin-lattice NMR relaxometry has been shown to nondestructively evaluate asphalt properties in situ through the analysis of hydrogen environments. The molecular mobility of hydrogen environments and with it the stiffness of asphalt binder samples can be determined by characteristic T1 relaxation times, indicating the complexity of asphalt-binder aging. In this study, two laboratory-generated asphalt mixtures, a failed field sample, and several laboratory-aged binder samples are compared by NMR relaxometry. NMR relaxometry was found to be able to differentiate between asphalt samples based on their binder percentage. According to the relaxometry findings, the RTFO binder aging compared favorably to the 6% laboratory-mixed sample. The PAV aging, however, did not compare well to the relaxometry results found for the field-aged sample. The amount of aggregate was found to have an influence on the relaxation times of the binder in the mixed samples and an inverse proportionality of the binder content to the primary NMR relaxation time was detected. It is concluded that molecular water present in the pores of the aggregate material gives rise to such a relationship. The findings of this study lay the foundation for nondestructive asphalt performance evaluation by NMR relaxometry. Full article
(This article belongs to the Section Solid-State Chemistry and Physics)
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<p>Research methodology.</p>
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<p>(<b>a</b>). Compacted HMA (<b>b</b>). Crushed HMA increasing in asphalt percent from left to right (4.5, field, 5.5, 6%).</p>
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<p>(<b>a</b>). Scatter plot of repeated 8 points (<b>b</b>). Device noise is the standard deviation (red bars) in mixtures and aggregate samples.</p>
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<p>(<b>a</b>). Viscoelastic comparison of binders (<b>b</b>). Primary T<sub>1</sub> relaxation time comparison of binders with standard deviation (red bars).</p>
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<p>Comparison of the 4.5%, field, 5.5%, and 6% HMA samples with standard deviation (red bars).</p>
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<p>T<sub>1</sub> comparison of the aggregate in normal, dry, and wet conditions with standard deviation (red bars).</p>
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<p>T<sub>1</sub> relaxation times from the biexponential fit of field HMA, lab HMA (4.5%, 5.5 6%), unaged binder, aged binders (PAV, RTFO), and aggregate (normal, dry, wet) with standard deviation (red bars).</p>
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18 pages, 1397 KiB  
Article
Applying Material Flow Analysis for Sustainable Waste Management of Single-Use Plastics and Packaging Materials in the Republic of Korea
by Hyeong-Jin Choi, Donggun Hwang, Young-Sam Yoon, Tae-Wan Jeon and Seung-Whee Rhee
Sustainability 2024, 16(16), 6926; https://doi.org/10.3390/su16166926 (registering DOI) - 13 Aug 2024
Abstract
This study involves a material flow analysis (MFA) of single-use plastics (SUPs) and packaging materials in the Republic of Korea, focusing on their short lifespans and significant contributions to plastic waste. Based on the MFA results, recommended policies for managing packaging materials and [...] Read more.
This study involves a material flow analysis (MFA) of single-use plastics (SUPs) and packaging materials in the Republic of Korea, focusing on their short lifespans and significant contributions to plastic waste. Based on the MFA results, recommended policies for managing packaging materials and SUPs were proposed. In 2021, 6.340 Mt of synthetic resin were produced, with 39.7% (2.518 Mt) utilized for packaging materials and SUPs. The per capita consumption of these materials was 48.7 kg/year, surpassing global averages. The separate collection rate was 54.6%, with films (26.2%) and manufacturing facilities (10.6%) exhibiting the lowest rates. The overall recycling rate was 52.7%, and 981 t of recycled waste was directly placed in soil. The reliability of the MFA results was estimated to be 83.1%, which is an improvement compared to previous studies. Recommendations include reducing plastic use, expanding recycling infrastructure, raising public awareness, and implementing stricter regulations to control soil contamination. Full article
(This article belongs to the Special Issue Sustainable Waste Management in the Context of Circular Economy)
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<p>Flowcharts explaining the scopes of material flow analysis (MFA) for packaging and single-use plastics (SUPs) conducted in this study. Abbreviations: polyethylene terephthalate (PET), low-density, polyethylene (LDPE), linear low-density polyethylene (LLDPE), high-density polyethylene (HDPE), polypropylene (PP), polystyrene (PS), polyvinyl chloride (PVC), polycarbonate (PC), expanded polystyrene (EPS).</p>
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<p>Results for material flow analysis (MFA) of packaging materials and single-use plastics (SUPs) conducted in this study. Abbreviations: polyethylene terephthalate (PET), low-density, polyethylene (LDPE), linear low-density polyethylene (LLDPE), high-density polyethylene (HDPE), polypropylene (PP), polystyrene (PS), polyvinyl chloride (PVC), polycarbonate (PC), and expanded polystyrene (EPS).</p>
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<p>Treatment of packaging and single-use plastics (SUPs) in the Republic of Korea: (<b>a</b>) mixed collected amount of packaging and SUPs; (<b>b</b>) separately collected amount of packaging and SUPs; and (<b>c</b>) ratio of packaging and SUPs by treatment (recycling, incineration, landfill, others). Abbreviations: polyethylene terephthalate (PET), expanded polystyrene (EPS).</p>
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14 pages, 2968 KiB  
Article
Effect of Sulfuric Acid Immersion on Electrical Insulation and Surface Composition of Amorphous Carbon Films
by Kazuya Kanasugi, Eito Ichijo, Masanori Hiratsuka and Kenji Hirakuri
Coatings 2024, 14(8), 1023; https://doi.org/10.3390/coatings14081023 - 12 Aug 2024
Viewed by 168
Abstract
Sulfuric acid is a concern for contacts within electronic devices, and the application of amorphous carbon films as thin electrical insulating coatings for small coils requires full investigation of its effects. Five types of amorphous carbon films were fabricated on Si substrates under [...] Read more.
Sulfuric acid is a concern for contacts within electronic devices, and the application of amorphous carbon films as thin electrical insulating coatings for small coils requires full investigation of its effects. Five types of amorphous carbon films were fabricated on Si substrates under different deposition conditions using vacuum coating systems. Based on their optical constants (ISO 23216:2021(E)), the films were classified into three types: hydrogenated amorphous carbon (a-C:H), polymer-like carbon (PLC), and graphite-like carbon (GLC). The structure, surface composition, and electrical insulation properties of the films were evaluated before and after immersion in sulfuric acid. Although the PLC and a-C:H showed progression of surface oxidation due to sulfuric acid immersion, none showed obvious changes in their structure or DC dielectric breakdown field strength due to sulfuric acid immersion, proving their stability. Furthermore, the PLC and a-C:H, which had a relatively low extinction coefficient, exhibited excellent insulation properties. Our results suggest that amorphous carbon films can be useful as thin insulating films for small coils that may come in contact with sulfuric acid. Our study offers a valuable tool for general users in the industry to facilitate selection of electrical insulating amorphous carbon films based on optical constants, such as extinction coefficients. Full article
(This article belongs to the Special Issue Thin Films and Coatings for Energy Storage and Conversion)
16 pages, 11008 KiB  
Article
Surface Development of Polyethylene Terephthalate Films Using Low-Pressure, High-Frequency Argon + Oxygen Plasma on Zinc Powder for Dye-Sensitized Solar Cells
by Wittawat Poonthong, Narong Mungkung, Khanchai Tunlasakun, Nuttee Thungsuk, Nat Kasayapanand, Somchai Arunrungrusmi, Tanes Tanitteerapan, Threerapong Maneepen, Apidat Songruk and Toshifumi Yuji
Polymers 2024, 16(16), 2283; https://doi.org/10.3390/polym16162283 - 12 Aug 2024
Viewed by 234
Abstract
This research has developed a process for producing ZnO thin film from DEZn deposited onto a PET substrate with low-pressure, high-frequency Ar + O2 plasma using a chemical vapor deposition technique. The aim is to study the film production conditions that affect [...] Read more.
This research has developed a process for producing ZnO thin film from DEZn deposited onto a PET substrate with low-pressure, high-frequency Ar + O2 plasma using a chemical vapor deposition technique. The aim is to study the film production conditions that affect electrical properties, optical properties, and thin film surfaces. This work highlights the use of plasma energy produced from a mixture of gases between Ar + O2. Plasma production is stimulated by an RF power supply to deliver high chemical energy and push ZnO atoms from the cathode inside the reactor onto the substrate through surface chemical reactions. The results showed that increasing the RF power in plasma production affected the chemical reactions on the substrate surface of film formations. Film preparation at an RF power of 300 W will result in the thickest films. The film has a continuous columnar formation, and the surface has a granular structure. This results in the lowest electrical resistivity of 1.8 × 10−4 Ω. In addition, when fabricated into a DSSC device, the device tested the PCE value and showed the highest value at 5.68%. The reason is due to the very rough surface nature of the ZnO film, which increases the scattering and storage of sunlight, making cells more efficient. Therefore, the benefit of this research is that it will be a highly efficient prototype of thin film production technology using a chemical process that reduces production costs and can be used in the industrial development of solar cells. Full article
(This article belongs to the Section Polymer Composites and Nanocomposites)
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<p>Equipment used in the low-pressure, high-frequency Ar + O<sub>2</sub> plasma using chemical vapor deposition technique of ZnO film fabrication on PET substrates.</p>
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<p>Reaction systems involving clusters of ZnO film formation under low-pressure, high-frequency plasma stimulation by low-pressure, high-frequency Ar + O<sub>2</sub> plasma chemical vapor deposition on a PET substrate.</p>
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<p>Influence of the variation RF power on ZnO film thickness prepared by low−pressure, high−frequency Ar + O<sub>2</sub> plasma chemical vapor deposition technique.</p>
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<p>X-ray diffraction analysis (XRD) of ZnO thin film deposited on a PET substrate prepared by low-pressure, high-frequency Ar + O<sub>2</sub> plasma chemical vapor deposition.</p>
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<p>Microstructure image of the ZnO thin film deposited on PET substrate under different conditions of RF power range of 200–300 W prepared by low-pressure, high-frequency Ar + O<sub>2</sub> plasma chemical vapor deposition: (<b>a</b>) FE-SEM images of top-view; (<b>b</b>) FE-SEM images of cross-section view; (<b>c</b>) AFM images.</p>
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<p>X-ray photoelectron spectroscopy spectra of ZnO thin films deposited on PET substrates with narrow scanning spectroscopy of Zn 2p.</p>
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<p>X-ray photoelectron spectroscopy spectra of ZnO thin films deposited on PET substrates with narrow scanning spectroscopy of O1s.</p>
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<p>Electrical resistivity of ZnO thin film deposited on PET substrate comparing by different low-pressure, high-frequency Ar + O<sub>2</sub> plasma supply with an RF power range of 200–300 W.</p>
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<p>Comparison the carrier mobility on ZnO thin film preparing at different conditions with an RF power range of 200–300 W under low-pressure, high-frequency Ar + O<sub>2</sub> plasma of chemical vapor deposition.</p>
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<p>Comparison the carrier concentration on ZnO thin film preparing at different conditions of an RF power range of 200–300 W under low-pressure, high-frequency Ar + O<sub>2</sub> plasma of chemical vapor deposition.</p>
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<p>Light transmittance of ZnO thin film deposited on PET substrate preparing by low-pressure, high-frequency Ar + O<sub>2</sub> plasma chemical vapor deposition under different conditions with an RF power range of 200–300 W.</p>
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<p>Photocurrent density-photovoltage (J–V) curves of DSSCs based on ZnO/PET substrates.</p>
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11 pages, 3160 KiB  
Article
Ferroelectric and Structural Properties of Cobalt-Doped Lead Ferrite Thin Films Formed by Reactive Magnetron Sputtering
by Benas Beklešovas, Vytautas Stankus, Aleksandras Iljinas and Liutauras Marcinauskas
Crystals 2024, 14(8), 721; https://doi.org/10.3390/cryst14080721 (registering DOI) - 12 Aug 2024
Viewed by 189
Abstract
Cobalt-doped lead ferrite (Pb2Fe2O5) thin films were deposited by reactive magnetron sputtering. The influence of the cobalt concentration and synthesis temperature on the structure, phase composition and ferroelectric properties of Pb2Fe2O5 thin [...] Read more.
Cobalt-doped lead ferrite (Pb2Fe2O5) thin films were deposited by reactive magnetron sputtering. The influence of the cobalt concentration and synthesis temperature on the structure, phase composition and ferroelectric properties of Pb2Fe2O5 thin films was investigated. It was determined that the increase in deposition temperature increased the grain size and density of the Co-doped PFO thin films. The XRD data demonstrated that the Co-doped Pb2Fe2O5 thin films consisted of Pb2Fe2O5 and PbO phases with a low amount of CoO and Co3O4 phases. The increase in the cobalt concentration in the Pb2Fe2O5 films slightly enhanced the cobalt oxide phase content. Polarization dependence on electric field measurement demonstrated that the highest ferroelectric properties of the Co-doped Pb2Fe2O5 films were obtained when the synthesis was performed at 550 °C temperatures. The increase in the cobalt concentration in the films enhanced the remnant polarization and coercive field values. It was found that the Co-doped Pb2Fe2O5 film deposited at 550 °C temperature and containing 10% cobalt had the highest remnant polarization (72 µC/cm2) and coercive electric field (105 kV/cm). Full article
(This article belongs to the Special Issue Magnetoelectric Materials and Their Application)
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<p>The XRD pattern of the Co-doped PFO thin films synthesized at 550 °C.</p>
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<p>XRD spectra of PFOCo10 films deposited at different temperatures.</p>
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<p>SEM images and cross-section views of PFOCo10 films deposited at (<b>a</b>,<b>d</b>) 500 °C, (<b>b</b>,<b>e</b>) 550 °C and (<b>c</b>,<b>f</b>) 600 °C.</p>
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<p>EDX mapping images of the PFOCo10 film deposited at 550 °C temperature.</p>
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<p>Comparison of the influence of cobalt content on the PFO P-E curves at different synthesis temperatures: (<b>a</b>) 500 °C; (<b>b</b>) 550 °C; (<b>c</b>) 600 °C.</p>
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<p>Effect of cobalt concentration on ferroelectric properties of PFO films deposited at (<b>a</b>) 500 °C; (<b>b</b>) 550 °C and (<b>c</b>) 600 °C temperatures.</p>
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18 pages, 6817 KiB  
Article
Effect of Water Tank Size and Supply on Greenhouse-Grown Kidney Beans Irrigated by Rainwater in Cold and Arid Regions of North China
by Mengmeng Sun, Jizong Zhang, Zhihui Wang, Jingxin Ran, Yunjie Han, Jianheng Zhang, Huibin Li and Lifeng Zhang
Agronomy 2024, 14(8), 1767; https://doi.org/10.3390/agronomy14081767 - 12 Aug 2024
Viewed by 185
Abstract
In response to water scarcity in the Bashang area of northwest Hebei Province, a cold and arid region in north China, and to address the diminishing groundwater levels caused by pumping irrigation, this study investigated the impact of rainwater tank size and water [...] Read more.
In response to water scarcity in the Bashang area of northwest Hebei Province, a cold and arid region in north China, and to address the diminishing groundwater levels caused by pumping irrigation, this study investigated the impact of rainwater tank size and water supply on kidney beans production in greenhouses under various precipitation scenarios to determine the production potential and development strategies for regional precipitation resources. Under the background of average annual precipitation, kidney bean yield increased with increasing reservoir volume and shorter irrigation cycles. Under a 4-day irrigation cycle, the water demand satisfaction rate of kidney beans reached 100% water demand when the rainwater tank size was 15.7 m3. Against the wide variation in multi-year regional precipitation from 1992 to 2023, the annual effect of rainwater harvest was simulated using precipitation data collected 20 years with an 80% precipitation guarantee rate. The average minimum yield reduction rate obtained was 9.4%, and the corresponding minimum rainwater tank size was 29.5 m3. By superimposing the rainwater harvested in the shed and nonshed areas, the volume of the reservoir without yield reduction could be reduced to 20.0 m3. The sum of discharged and inventory water was much greater than the water scarcity in each water supply situation. Simulating and analyzing the effect of the relationship between rainwater tank size and water supply on rainwater harvesting in regional farmland by year provides important data affecting the construction of regional rainwater storage facilities and water supply efficiency. To achieve a high, stable yield of kidney beans grown in a greenhouse with shed film and shed area rainwater harvesting in north China, 2.6 m3 supplementary groundwater irrigation is still needed during the annual growing season. Full article
(This article belongs to the Section Farming Sustainability)
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<p>Location of the research area.</p>
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<p>Greenhouse rainwater harvesting, storage, and utilization system.</p>
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<p>Rainwater tank size under the average daily rainfall of 25 years and reference irrigation scheme scenario-water supply effect.</p>
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<p>Water demand satisfaction rate of the 8.0 m<sup>3</sup> rainwater tank of the kidney bean greenhouse.</p>
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<p>Influence of irrigation cycle (irrigation frequency) on water supply for an 8.0 m<sup>3</sup> rainwater tank.</p>
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22 pages, 8397 KiB  
Article
A Polymer Thick Film on an Organic Substrate Grid Electrode and an Open-Source Recording System for UHF MRI: An Imaging Study
by Yinching Iris Chen, Ilknur Ay, Francesca Marturano, Peter Fuller, Hernan Millan and Giorgio Bonmassar
Sensors 2024, 24(16), 5214; https://doi.org/10.3390/s24165214 (registering DOI) - 12 Aug 2024
Viewed by 183
Abstract
Electrocorticography (ECoG) is a critical tool in preclinical neuroscience research for studying global network activity. However, integrating ECoG with functional magnetic resonance imaging (fMRI) has posed challenges, due to metal electrode interference with imaging quality and heating around the metallic electrodes. Here, we [...] Read more.
Electrocorticography (ECoG) is a critical tool in preclinical neuroscience research for studying global network activity. However, integrating ECoG with functional magnetic resonance imaging (fMRI) has posed challenges, due to metal electrode interference with imaging quality and heating around the metallic electrodes. Here, we introduce recent advancements in ECoG grid development that utilize a polymer-thick film on an organic substrate (PTFOS). PTFOS offers notable advantages over traditional ECoG grids. Firstly, it significantly reduces imaging artifacts, ensuring minimal interference with MR image quality when overlaying brain tissue with PTFOS grids. Secondly, during a 30-min fMRI acquisition, the temperature increase associated with PTFOS grids is remarkably low, measuring only 0.4 °C. These findings suggest that utilizing ECoG with PTFOS grids has the potential to enhance the safety and efficacy of neurosurgical procedures. By providing clearer imaging results and mitigating risk factors such as excessive heating during MRI scans, PTFOS-based ECoG grids represent a promising advancement in neurosurgical technology. Furthermore, we describe a cutting-edge open-source system designed for simultaneous electrophysiology and fMRI. This system stands out due to its exceptionally low input noise levels (<0.6 V peak-to-peak), robust electromagnetic compatibility (it is suitable for use in MRI environments up to 9.4 teslas), and the inclusion of user-programmable real-time signal-processing capabilities. The open-platform software is a key feature, enabling researchers to swiftly implement and customize real-time signal-processing algorithms to meet specific experimental needs. This innovative system has been successfully utilized in several rodent EEG/fMRI studies, particularly at magnetic field strengths of 4.7 and 9.4 teslas, focusing on the somatosensory system. These studies have allowed for detailed observation of neural activity and responses within this sensory system, providing insights that are critical for advancing our understanding of neurophysiological processes. The versatility and high performance of our system make it an invaluable tool for researchers aiming to integrate and analyze complex datasets from advanced imaging and electrophysiological recordings, ultimately enhancing the depth and scope of neuroscience research. Full article
(This article belongs to the Section Physical Sensors)
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<p>Susceptibility artifact induced by a Pt wire (common implant wires) in a phantom on an ultra-high magnetic field MRI (9.4 T).</p>
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<p>The PTFOS. (<b>a</b>) Image of the 32 electrodes and the connector. (<b>b</b>) The PTFOS layout is based on an absorbable gelatin film made from denatured collagen (Gelfilm by Pharmacia and Upjohn Co, Division of Pfizer Inc., New York City, NJ, USA).</p>
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<p>HF-2 system architectural diagram [<a href="#B7-sensors-24-05214" class="html-bibr">7</a>]. HF-2 is composed of four boards inside a shielded enclosure, with an external preamplification board. Below is an image of the HF-2 system and the battery.</p>
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<p>HF-2 hardware [<a href="#B7-sensors-24-05214" class="html-bibr">7</a>]: (<b>a</b>) preamplification board, (<b>b</b>) analog board, (<b>c</b>) clock board, and (<b>d</b>) CPU board.</p>
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<p>Real-Time software.</p>
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<p>Windows LabVIEW: (<b>a</b>) Host interface showing screenshots obtained from the user interface in a rat experiment. The PTFOS was implanted into the right sensory S1 cortex, and stimulation electrodes were placed in the right and left forelimbs and hindlimbs. (<b>b</b>) The review panel will look at the existing recordings (i.e., sinusoid). (<b>c</b>) Status bar.</p>
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<p>The temperature test of the PTFOS.</p>
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<p>In vivo images of the rat with the PTFOS and connector implanted at 9.4 T, showing only minimal artifacts near the electrodes.</p>
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<p>SNR comparison of T2-weighted images of rats with (<b>a</b>) sham Gelfilm, (<b>b</b>) PTFOS and a connector, and (<b>c</b>) PTFOS without a connector. (<b>d</b>) The SNR projection, from the top to the bottom of the head. The SNR on the top portion of the brain was relatively smooth and homogeneous with the PTFOS with a connector, compared to the ones without the connector or with sham Gelfilm.</p>
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<p>The 9.4 T fMRI with electrical forepaw stimulation (1.5 mA/2 Hz) on a rat with PTFOS implanted. (<b>a</b>) The colormap representing the brain area, with statistically significant BOLD responses to the forepaw stimulation. (<b>b</b>) The BOLD time course in response to the electrical forepaw stimulation (yellow block).</p>
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<p>Shielding of the HF-2, showing the effect on EPI (fMRI) images at 4.7 T: (<b>a</b>) System ON and Shielding OFF, and (<b>b</b>) System and Shielding ON.</p>
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<p>Synchronized vs. out-of-synchronization recordings of HF-2 with a phantom at 4.7 T (Brucker), using EPI. (<b>a</b>) Eight channels of HF-2 recordings, with the system clock synchronized to the 4.7 T MRI scanner. (<b>b</b>) Recordings without synchronization to the MRI’s master clock. These raw data illustrate that without synchronization, the recording is affected by more EPI noise and more variance.</p>
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<p>The spectrogram of a sinusoid acquired with HF2 (blue) and Biopac (orange). The Biopac system has a higher noise floor and exhibits more noise peaks.</p>
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<p>Tissue reactivity of PTFOS compared to Gelfilm<sup>®</sup> and a conventional grid. H&amp;E panel shows greater tissue disruption (arrow) from the standard grid as compared to Gelfilm<sup>®</sup> or PTFOS. Fluoro-Jade panel shows bright lines of injured cells in the cortex (arrow) in contact with the standard grid as well as patches of injured cells in subcortical tissues (arrowheads). White dots indicate the interface between the implant and the cortical surface. Minimal injury is seen in the images of the tissues in contact with Gelfilm<sup>®</sup> and PTFOS. NeuN panel shows lower density of neuronal nuclei in the cortex in contact with the conventional grid as compared to Gelfilm<sup>®</sup> and PTFOS (compare the density of nuclei inside the frames). IBA-1 panel shows higher density of microglia in the cortex in contact with the conventional grid as compared to Gelfilm<sup>®</sup> and PTFOS (the arrow shows an area of microglia accumulation). Silver panel shows more disruption of cortical nerve fibers (arrow) from the conventional grid as compared to Gelfilm<sup>®</sup> or PTFOS. The images of the tissue neighboring PTFOS and Gelfilm<sup>®</sup> appear the same across all staining methods. This figure was previously reported in Radiology [<a href="#B2-sensors-24-05214" class="html-bibr">2</a>].</p>
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<p>Microstructural stability of PTFOS implants. We implanted 5mm disks of PTFOS over the cortex of two mice (<b>A</b>). After 30 days, we harvested the PTFOS implant (<b>B</b>) and imaged it using a scanning electron microscope (<b>C</b>). For comparison, we also imaged a PTFOS disk that was not implanted (<b>D</b>). We used high-magnification levels, enabling us to see the PTFOS microstructure with the scale of 10 μm (<b>E</b>,<b>F</b>), to search selected areas of electrodes (arrows) and conductive lines (arrowheads) for the presence of breaks/cracks. We did not find any breaks/cracks in the electrodes/conductive lines of the PTFOS implants that were and were not implanted. This figure was previously reported in Radiology [<a href="#B2-sensors-24-05214" class="html-bibr">2</a>].</p>
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28 pages, 5188 KiB  
Review
Enhanced Multifaceted Properties of Nanoscale Metallic Multilayer Composites
by Mahmoud Ebrahimi, Bangcai Luo, Qudong Wang and Shokouh Attarilar
Materials 2024, 17(16), 4004; https://doi.org/10.3390/ma17164004 - 12 Aug 2024
Viewed by 270
Abstract
This study explored the fascinating field of high-performance nanoscale metallic multilayer composites, focusing on their magnetic, optical, and radiation tolerance properties, as well as their thermal and electrical properties. In general, nanoscale metallic multilayer composites have a wide range of outstanding properties, which [...] Read more.
This study explored the fascinating field of high-performance nanoscale metallic multilayer composites, focusing on their magnetic, optical, and radiation tolerance properties, as well as their thermal and electrical properties. In general, nanoscale metallic multilayer composites have a wide range of outstanding properties, which differ greatly from those observed in monolithic films. Their exceptional properties are primarily due to the large number of interfaces and nanoscale layer thicknesses. Through a comprehensive review of existing literature and experimental data, this paper highlights the remarkable performance enhancements achieved by the precise control of layer thicknesses and interfaces in these composites. Furthermore, it will discuss the underlying mechanisms responsible for their exceptional properties and provide insights into future research directions in this rapidly evolving field. Many studies have investigated these materials, focusing on their magnetic, mechanical, optical, or radiation-tolerance properties. This paper summarizes the findings in each area, including a description of the general attributes, the adopted synthesis methods, and the most common characterization techniques used. The paper also covers related experimental data, as well as existing and promising applications. The paper also covers other phenomena of interest, such as thermal stability studies, self-propagating reactions, and the progression from nanomultilayers to amorphous and/or crystalline alloys. Finally, the paper discusses challenges and future perspectives relating to nanomaterials. Overall, this paper is a valuable resource for researchers and engineers interested in harnessing the full potential of nanoscale metallic multilayer composites for advanced technological applications. Full article
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<p>The evolution roadmap of nanoscale metallic multilayer composites (NMMCs).</p>
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<p>Superparamagnetic supraparticles. (<b>a</b>) The experimental setup for the evaporation-guided assembly of a magnetic nanoparticle dispersion on a superamphiphobic surface that produces supraparticles, and (<b>b</b>) the drying process of a 3% weight droplet in the absence (<b>upper</b> panel) and presence (<b>bottom</b> panel) of a magnetic field. Note that a 0.5 mm scale bar is used [<a href="#B57-materials-17-04004" class="html-bibr">57</a>].</p>
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<p>AFM image showing magnetic islands with diameters of 140 and 500 nm within a nonmagnetic matrix following patterning. Note that the Ar<sup>+</sup> implantation has caused the matrix regions to enlarge by around 10 nm in height relative to the protected islands [<a href="#B69-materials-17-04004" class="html-bibr">69</a>].</p>
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<p>Unfolded Fermi surface WSe<sub>2</sub> monolayer from the Fe/WSe2/Pt heterostructure along with its structure and spin Seebeck coefficient (<span class="html-italic">S</span><sub>spin</sub>) as a function of chemical potential (<span class="html-italic">μ</span>) [<a href="#B71-materials-17-04004" class="html-bibr">71</a>].</p>
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<p>Diagram showing ferromagnetic A and non-magnetic B layers in magnetic multilayers. Note that d and d′ indicate the layer’s thickness.</p>
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<p>The schematic representation of (<b>a</b>) conventional silica–gold core nanoshells, (<b>b</b>) multilayer gold–silica–gold nanoshells, and (<b>c</b>) conventional silica–gold core and multilayer gold–silica–gold nanoshell calculated spectra with different inner core radii but the silica and outer radii staying the same (Media 1). Note that the lambda shift indicates the multilayer gold–silica–gold nanoshells’ red shift from the conventional silica–gold core nanoshells [<a href="#B85-materials-17-04004" class="html-bibr">85</a>].</p>
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<p>The structural characteristics of nanocomposite Ag-SiO<sub>2</sub> films and the effect of altering co-sputtering duration at film thicknesses [<a href="#B87-materials-17-04004" class="html-bibr">87</a>].</p>
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<p>Analysis of fringe patterns: (<b>a</b>) the diagram illustrates the exciton transition dipole’s schematic representation, with the top figure showing its out-of-plane orientation and the bottom figure demonstrating its inclined angle; (<b>b</b>) the near-field emission wavelength map of Al<sub>2</sub>O<sub>3</sub> (5 nm)/NP/Au is displayed with a topography background; (<b>c</b>) the line-cuts of TEPL intensity at various direction angles; and (<b>d</b>) the fringe period expressed mathematically as a function of the angle. Note that the error bar corresponds to the full width at half maximum (FWHM) of the peak observed in the Fourier transform of the fringe profiles in (<b>c</b>). The scale bar represents 0.5 µm [<a href="#B91-materials-17-04004" class="html-bibr">91</a>].</p>
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<p>Production of monometallic and multimetallic alloy nanoparticles, as well as the simultaneous effects of sublimation, dewetting, and interdiffusion. (<b>a</b>) Diagrams showing how Ag/Pt and Ag/Au/Pt multilayers are deposited on sapphire (0001) (atomic diffusion at low temperatures during annealing (a-1)), (<b>b</b>) sublimation of Ag atoms while alloy nanoparticles (NPs) are formed, (<b>c</b>) Pt and AuPt NP formation following Ag sublimation, (<b>d</b>) extinction rates of common AgPt and Pt NPs are compared, and (<b>e</b>) local e-field distribution using finite difference time domain (FDTD) simulation of a typical Pt NP [<a href="#B102-materials-17-04004" class="html-bibr">102</a>].</p>
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<p>Schematic representation of the operating principle of the Co-OEC/(AuNP/TNP)n photoanode [<a href="#B103-materials-17-04004" class="html-bibr">103</a>].</p>
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<p>The thermal conductivity of Cu/W multilayered nanofilms at room temperature with varying periodic thicknesses, along with bright-field cross-sectional TEM images of the Cu/W multilayered nanofilms: (<b>a1</b>) thermal conductivity of Cu/W multilayered nanofilms curves at room temperature according to varied periodic thicknesses; (<b>a2</b>) structure of Cu/W multilayered nanofilms; (<b>a3</b>) bright-field cross-sectional TEM micrographs of the Cu/W multilayered nanofilms [<a href="#B106-materials-17-04004" class="html-bibr">106</a>].</p>
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<p>Schematic of the thermal resistance of the Al-Ir-MgO material stack [<a href="#B113-materials-17-04004" class="html-bibr">113</a>].</p>
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<p>Thermal transport physics schematics across the interface. (<b>a</b>) Heat dissipation in a large-scale integrated circuit and (<b>b</b>) phonon transport at the interface of materials A and B [<a href="#B115-materials-17-04004" class="html-bibr">115</a>].</p>
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21 pages, 13582 KiB  
Article
Fabrication of Silica–Titanium Composite Film on Wood Surface and Optimization of Its Structure and Properties
by Zhigao Liu, Qianying Li, Si Cheng, Penglian Wei and Yunlin Fu
Forests 2024, 15(8), 1410; https://doi.org/10.3390/f15081410 - 12 Aug 2024
Viewed by 205
Abstract
In this thesis, wood loaded with a silica–titanium (Si-Ti) composite film was prepared using the sol–gel method in order to achieve improved wood with high hydrophobicity and photocatalytic activity under visible light. The factors affecting the structure and properties of the composite film, [...] Read more.
In this thesis, wood loaded with a silica–titanium (Si-Ti) composite film was prepared using the sol–gel method in order to achieve improved wood with high hydrophobicity and photocatalytic activity under visible light. The factors affecting the structure and properties of the composite film, as well as the optimization process, were discussed. Infrared analysis revealed that the vibrational intensity of Si-O-Si, Ti-O-Ti, and Ti-O-Si telescopic vibration peaks increased with an increase in vinyltriethoxysilane (VETS). Additionally, the number of Ti-O-Ti telescopic vibration peaks also increased with an increase in VETS. Furthermore, the intensity of -NO3, Si-O-Si, and Ti-O-Ti telescopic vibrational peaks was enhanced with a higher dosage of nitric acid. Conversely, the intensity of -OH telescopic vibrational peaks decreased with an increase in drying temperature. XRD analysis showed that nitric acid could promote the transformation of TiO2 from amorphous to anatase, while SiO2 would reduce the grain size of anatase TiO2 and promote the growth of rutile TiO2. Additionally, wood surfaces loaded with Si-Ti composite film changed from hydrophilic to hydrophobic, with significant differences observed between different levels of each factor. The photocatalytic activity of surface-loaded Si-Ti composite films on wood was most affected by the amount of nitric acid, which influenced crystallinity of TiO2 and thus impacted the photocatalytic activity. Furthermore, changes in VTES dosage not only affected the crystalline phase of TiO2 and the grain size of Si-Ti composite film but also influenced the crystallinity of TiO2 through generating SiO2. Finally, based on optimal preparation process (titanium–alcohol ratio of 1:5, titanium–silicon ratio of 1:0.2, titanium–acid ratio of 1:0.5, and drying temperature of 100 °C), wood surfaces loaded with Si-Ti composite film achieved a contact angle up to 125.9° and exhibited a decolorization rate for rhodamine B under UV light reaching 94% within 180 min. Full article
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<p>The standard curve of Rhodamine B aqueous solution.</p>
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<p>The FTIR spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(EtOH).</p>
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<p>The XRD spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(EtOH).</p>
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<p>The contact angle of Si-Ti composite film prepared at different ratios of n(TBOT) to n(EtOH).</p>
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<p>The Fisher LSD multiple comparison of wettability of Si-Ti composite film prepared at different ratios of n(TBOT) to n(EtOH). Note: The lowercase and uppercase letters indicate the significance at <span class="html-italic">p</span> &lt; 0.05, <span class="html-italic">p</span> &lt; 0.01, respectively. The error bars show the mean ± standard deviation.</p>
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<p>The decolorization rate of RhB of Si-Ti composite film prepared at different ratios of n(TBOT) to n(EtOH).</p>
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<p>The FTIR spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(VETS).</p>
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<p>The XRD spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(VETS).</p>
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<p>The contact angle of Si-Ti composite film prepared at different ratios of n(TBOT) to n(VETS).</p>
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<p>The Fisher LSD multiple comparison of Si-Ti composite film prepared at different ratios of n(TBOT) to n(VETS). Note: The lowercase and uppercase letters indicate the significance at <span class="html-italic">p</span> &lt; 0.05, <span class="html-italic">p</span> &lt; 0.01, respectively. The error bars show the mean ± standard deviation.</p>
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<p>The decolorization rate of RhB of Si-Ti composite film prepared at different ratios of n(TBOT) to n(VETS).</p>
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<p>The FTIR spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(HNO<sub>3</sub>).</p>
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<p>The XRD spectrum of Si-Ti composite film prepared at different ratios of n(TBOT) to n(HNO<sub>3</sub>).</p>
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<p>The contact angle of Si-Ti composite film prepared at different ratios of n(TBOT) to n(HNO<sub>3</sub>).</p>
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<p>The Fisher LSD multiple comparison of wettability of Si-Ti composite film prepared at different ratios of n(TBOT) to n(HNO<sub>3</sub>). Note: The lowercase and uppercase letters indicate the significance at <span class="html-italic">p</span> &lt; 0.05, <span class="html-italic">p</span> &lt; 0.01, respectively. The error bars show the mean ± standard deviation.</p>
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<p>The decolorization rate of RhB of Si-Ti composite film prepared at different ratios of n(TBOT) to n(HNO<sub>3</sub>).</p>
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<p>The FTIR spectrum of Si-Ti composite film prepared at different drying temperatures.</p>
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<p>The XRD spectrum of Si-Ti composite film prepared at different drying temperatures.</p>
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<p>The contact angle of Si-Ti composite film prepared at different drying temperatures.</p>
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<p>The Fisher LSD multiple comparison of Si-Ti composite film prepared at different drying temperatures. Note: The lowercase and uppercase letters indicate the significance at <span class="html-italic">p</span> &lt; 0.05, <span class="html-italic">p</span> &lt; 0.01, respectively. The error bars show the mean ± standard deviation.</p>
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<p>The decolorization rate of RhB of Si-Ti composite film prepared at different drying temperatures.</p>
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29 pages, 10900 KiB  
Review
Recent Developments of Pineapple Leaf Fiber (PALF) Utilization in the Polymer Composites—A Review
by Murugan Sethupathi, Mandla Vincent Khumalo, Sifiso John Skosana and Sudhakar Muniyasamy
Separations 2024, 11(8), 245; https://doi.org/10.3390/separations11080245 - 12 Aug 2024
Viewed by 286
Abstract
Plant fibers’ wide availability and accessibility are the main causes of the growing interest in sustainable technologies. The two primary factors to consider while concentrating on composite materials are their low weight and highly specific features, as well as their environmental friendliness. Pineapple [...] Read more.
Plant fibers’ wide availability and accessibility are the main causes of the growing interest in sustainable technologies. The two primary factors to consider while concentrating on composite materials are their low weight and highly specific features, as well as their environmental friendliness. Pineapple leaf fiber (PALF) stands out among natural fibers due to its rich cellulose content, cost-effectiveness, eco-friendliness, and good fiber strength. This review provides an intensive assessment of the surface treatment, extraction, characterization, modifications and progress, mechanical properties, and potential applications of PALF-based polymer composites. Classification of natural fibers, synthetic fibers, chemical composition, micro cellulose, nanocellulose, and cellulose-based polymer composite applications have been extensively reviewed and reported. Besides, the reviewed PALF can be extracted into natural fiber cellulose and lignin can be used as reinforcement for the development of polymer biocomposites with desirable properties. Furthermore, this review article is keen to study the biodegradation of natural fibers, lignocellulosic biopolymers, and biocomposites in soil and ocean environments. Through an evaluation of the existing literature, this review provides a detailed summary of PALF-based polymer composite material as suitable for various industrial applications, including energy generation, storage, conversion, and mulching films. Full article
(This article belongs to the Special Issue Degradation and Separation of Fibre-Based Materials)
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<p>Image of <span class="html-italic">Ananas comosus</span> plants and pineapple leaf fibers.</p>
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<p>The natural fiber cell structural composition.</p>
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<p>Classification of natural and synthetic fibers (Gurunathan et al. [<a href="#B21-separations-11-00245" class="html-bibr">21</a>]).</p>
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<p>Nanocellulose is typically classified into three types based on its structure and properties.</p>
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<p>Shows the view of the wet fiber obtained after the extraction process.</p>
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<p>Illustration showing how the nanocrystalline cellulose is separated from pineapple crown leaf.</p>
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<p>FESEM of different treatments of pineapple leaves ((<b>a</b>) Bleached pineapple leaves (raw), (<b>b</b>) hydrolyzed pineapple leaves) (Ravindran et al. [<a href="#B53-separations-11-00245" class="html-bibr">53</a>]).</p>
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<p>(<b>a</b>,<b>b</b>) TEM image of cellulose nanofiber (Klinthoopthamrong et al. [<a href="#B52-separations-11-00245" class="html-bibr">52</a>]).</p>
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<p>Several applications for pineapple leaves in the present and the future.</p>
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<p>Classifications of the different biodegradable polymers.</p>
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<p>Classification of lignocellulosic composites.</p>
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21 pages, 34742 KiB  
Article
Integrating Depth-Based and Deep Learning Techniques for Real-Time Video Matting without Green Screens
by Pin-Chen Su and Mau-Tsuen Yang
Electronics 2024, 13(16), 3182; https://doi.org/10.3390/electronics13163182 - 12 Aug 2024
Viewed by 269
Abstract
Virtual production, a filmmaking technique that seamlessly merges virtual and real cinematography, has revolutionized the film and television industry. However, traditional virtual production requires the setup of green screens, which can be both costly and cumbersome. We have developed a green screen-free virtual [...] Read more.
Virtual production, a filmmaking technique that seamlessly merges virtual and real cinematography, has revolutionized the film and television industry. However, traditional virtual production requires the setup of green screens, which can be both costly and cumbersome. We have developed a green screen-free virtual production system that incorporates a 3D tracker for camera tracking, enabling the compositing of virtual and real-world images from a moving camera with varying perspectives. To address the core issue of video matting in virtual production, we introduce a novel Boundary-Selective Fusion (BSF) technique that combines the alpha mattes generated by deep learning-based and depth-based approaches, leveraging their complementary strengths. Experimental results demonstrate that this combined alpha matte is more accurate and robust than those produced by either method alone. Overall, the proposed BSF technique is competitive with state-of-the-art video matting methods, particularly in scenarios involving humans holding objects or other complex settings. The proposed system enables real-time previewing of composite footage during filmmaking, reducing the costs associated with green screen setups and simplifying the compositing process of virtual and real images. Full article
(This article belongs to the Special Issue Applications of Artificial Intelligence in Computer Vision)
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<p>Concept map of the proposed virtual production system with moving camera tracking in varying perspectives.</p>
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<p>Architecture of the proposed virtual production system.</p>
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<p>Camera video and tracking data flow diagram.</p>
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<p>Experimental environment of the proposed virtual production system including VIVE base station placement, camera tracking range, and foreground character active area.</p>
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<p>Depth-based video matting module.</p>
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<p>Flowchart of the proposed Boundary-Selective Fusion (BSF) and comparison of four alpha mattes. (<b>a</b>) Flowchart; (<b>b</b>) Alpha matte generated by deep learning-based module; (<b>c</b>) Alpha matte generated by depth-based module; (<b>d</b>) Combined alpha matte using the proposed BSF; (<b>e</b>) Ground truth. The source images are taken from the HDM-2K dataset [<a href="#B17-electronics-13-03182" class="html-bibr">17</a>].</p>
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<p>Occlusion handling via UI plane in Unity. (<b>a</b>) Image rendered in Unity scene; (<b>b</b>) Image properly rendered with occlusion considered.</p>
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<p><span class="html-italic">MAD error</span> over time of video matting in static background.</p>
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<p><span class="html-italic">MAD error</span> over time of video matting in dynamic foreground with humans holding an object.</p>
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<p>Initial camera position and composite image. (<b>a</b>) Initial virtual camera position (Unity coordinates); (<b>b</b>) Initial composite image with real-world human and virtual background.</p>
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<p>Some video compositing results of the virtual production system. (<b>a</b>) Sci-fi office background; (<b>b</b>) Outdoor background; (<b>c</b>–<b>f</b>) depicts a sequence of shots manipulating different times of a day.</p>
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<p>Occlusion effect of the virtual production system. (<b>a</b>) The virtual object closer to the camera than the real-world human; (<b>b</b>) The virtual object occludes the real-world human; (<b>c</b>) The real-world human closer to the camera than the virtual object; (<b>d</b>) The real-world human occludes the virtual object.</p>
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<p>User interface of the virtual production system.</p>
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