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17 pages, 3640 KiB  
Article
WO3−x/WS2 Nanocomposites for Fast-Response Room Temperature Gas Sensing
by Svetlana S. Nalimova, Zamir V. Shomakhov, Oksana D. Zyryanova, Valeriy M. Kondratev, Cong Doan Bui, Sergey A. Gurin, Vyacheslav A. Moshnikov and Anton A. Zhilenkov
Molecules 2025, 30(3), 566; https://doi.org/10.3390/molecules30030566 (registering DOI) - 26 Jan 2025
Abstract
Currently, semiconductor gas sensors are being actively studied and used in various fields, including ecology, industry, and medical diagnostics. One of the major challenges is to reduce their operating temperature to room temperature. To address this issue, sensor layers based on WO3−x [...] Read more.
Currently, semiconductor gas sensors are being actively studied and used in various fields, including ecology, industry, and medical diagnostics. One of the major challenges is to reduce their operating temperature to room temperature. To address this issue, sensor layers based on WO3−x/WS2 nanostructures synthesized by the hydrothermal method have been proposed. In this paper, the morphology of the material’s surface and its elemental composition were investigated, as well as the optical band gap. Additionally, changes in the resistance of the WO3−x/WS2 sensor layers under the influence of alcohol vapors at room temperature were analyzed. The results showed that the layers exhibited a significant response, with short response and recovery times. The achieved response value to 1000 ppm of isopropanol was 1.25, with a response time of 13 s and a recovery time of 12 s. The response to 1000 ppm of ethanol was 1.35, and the response and recovery times were 20 s. This indicates that these sensor layers have promising potential for various applications. Full article
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Figure 1
<p>(<b>a</b>) SEM image of WO<sub>3−x</sub>/WS<sub>2</sub> nanocomposite, (<b>b</b>) cleavage of substrate with WO<sub>3−x</sub>/WS<sub>2</sub> sensor layer.</p>
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<p>EDX spectrum of WO<sub>3−x</sub>/WS<sub>2</sub> nanocomposite.</p>
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<p>XPS spectra WO<sub>3−x</sub>/WS<sub>2</sub> nanostructure: survey (<b>a</b>), W 4f (<b>b</b>), O 1s (<b>c</b>), S 2p (<b>d</b>) levels.</p>
Full article ">Figure 3 Cont.
<p>XPS spectra WO<sub>3−x</sub>/WS<sub>2</sub> nanostructure: survey (<b>a</b>), W 4f (<b>b</b>), O 1s (<b>c</b>), S 2p (<b>d</b>) levels.</p>
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<p>Tauc plot of WO<sub>3−x</sub>/WS<sub>2</sub> nanocomposite.</p>
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<p>Sensor resistance when exposed to different target gases.</p>
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<p>Sensor response when exposed to different target gas concentrations.</p>
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<p>Response and recovery times of WO<sub>3−x</sub>/WS<sub>2</sub> nanocomposite when detecting (<b>a</b>) ethanol and (<b>b</b>) isopropanol.</p>
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<p>Influence of humidity on sensor resistance.</p>
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<p>Influence of relative humidity on the sensor response.</p>
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<p>The substrate used for depositing the sensor layer.</p>
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<p>Stages of WO<sub>3−x</sub>/WS<sub>2</sub> nanocomposite synthesis.</p>
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<p>System for generating vapor flows and measuring sensor gas properties.</p>
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19 pages, 2711 KiB  
Article
Implementing an Analytical Model to Elucidate the Impacts of Nanostructure Size and Topology of Morphologically Diverse Zinc Oxide on Gas Sensing
by Sanju Gupta and Haiyang Zou
Chemosensors 2025, 13(2), 38; https://doi.org/10.3390/chemosensors13020038 (registering DOI) - 26 Jan 2025
Abstract
The development of state-of-the-art gas sensors based on metal oxide semiconductors (MOS) to monitor hazardous and greenhouse gas (e.g., methane, CH4, and carbon dioxide, CO2) has been significantly advanced. Moreover, the morphological and topographical structures of MOSs have significantly [...] Read more.
The development of state-of-the-art gas sensors based on metal oxide semiconductors (MOS) to monitor hazardous and greenhouse gas (e.g., methane, CH4, and carbon dioxide, CO2) has been significantly advanced. Moreover, the morphological and topographical structures of MOSs have significantly influenced the gas sensors by means of surface catalytic activities. This work examines the impact of morphological and topological networked assembly of zinc oxide (ZnO) nanostructures, including microparticles and nanoparticles (0D), nanowires and nanorods (1D), nanodisks (2D), and hierarchical networks of tetrapods (3D). Gas sensors consisting of vertically aligned ZnO nanorods (ZnO–NR) and topologically interconnected tetrapods (T–ZnO) of varying diameter and arm thickness synthesized using aqueous phase deposition and flame transport method on interdigitated Pt electrodes are evaluated for methane detection. Smaller-diameter nanorods and tetrapod arms (nanowire-like), having higher surface-to-volume ratios with reasonable porosity, exhibit improved sensing behavior. Interestingly, when the nanorods’ diameter and interconnected tetrapod arm thickness were comparable to the width of the depletion layer, a significant increase in sensitivity (from 2 to 30) and reduction in response/recovery time (from 58 s to 5.9 s) resulted, ascribed to rapid desorption of analyte species. Additionally, nanoparticles surface-catalyzed with Pd (~50 nm) accelerated gas sensing and lowered operating temperature (from 200 °C to 50 °C) when combined with UV photoactivation. We modeled the experimental findings using a modified general formula for ZnO methane sensors derived from the catalytic chemical reaction between methane molecules and oxygen ions and considered the structural surface-to-volume ratios (S/V) and electronic depletion region width (Ld) applicable to other gas sensors (e.g., SnO2, TiO2, MoO3, and WO3). Finally, the effects of UV light excitation reducing detection temperature help to break through the bottleneck of ZnO-based materials as energy-saving chemiresistors and promote applications relevant to environmental and industrial harmful gas detection. Full article
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<p>Gas sensor development based on various ZnO morphologies. (<b>a</b>) Gas concentration sensing ranges depending upon the type of gas sensor. (<b>b</b>) Preferential growth direction of hexagonal ZnO wurtzite crystal shown with crystal facets and structures in dimensions from 3D to 0D typically grown along [0001] direction. Also shown are examples, diameter (D), and thickness (L) of nanostructures.</p>
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<p>Surface morphology of various nanoscale ZnO, crystal structure, and optical properties. (<b>A</b>) Schematic of semiconducting metal oxide (MOS) gas sensor as chemiresistor along with ZnO crystal structure with oxygen vacancy (V<sub>O</sub>) and interstitial Zn (I<sub>Zn</sub>) point defects. (<b>B</b>) FESEM images of ZnO structures: (<b>a</b>) Nanoparticles, NP; (<b>b</b>) Microparticles, MP; (<b>c</b>) Nanowires; (<b>d</b>) Nanorods (ZnO–NR); (<b>e</b>,<b>f</b>) Pdcat/ZnO–NR; (<b>g</b>) hierarchical tetrapods (T–ZnO); and (<b>h</b>) Pdcat/T–ZnO, thin film assembly. (<b>C</b>) (Top panels) X-ray diffractograms of ZnO–NR, Pdcat/ZnO–NR, T–ZnO, Pdcat/T–ZnO, showing characteristic peaks of ZnO. (<b>D</b>) (Bottom panels) Room temperature photoluminescence (PL) spectra of ZnO–NR, Pdcat/ZnO–NR, T–ZnO, and Pdcat/T–ZnO, showing light emission peaks related to surface oxygen vacancies and other intrinsic defects.</p>
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<p>Optimization of operating temperature and activation energy. (<b>a</b>) Representative semilog plot of <span class="html-italic">dc</span> conductivity with temperature in the dark and with UV A excitation (365 nm) for ZnO–NR<sub>1 and 2</sub>, Pd<sub>cat</sub>/ZnO–NR<sub>1 and 2</sub>, T–ZnO, and Pd<sub>cat</sub>/T–ZnO sensor films measured in synthetic air. (<b>b</b>) Corresponding activation energy summary table. The short, dotted lines in (<b>a</b>) are the linear fits.</p>
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<p>Performance of methane sensing from nanostructured ZnO. (<b>a</b>) log (S<sub>g</sub> − 1) versus log C<sub>g</sub> plot and (<b>b</b>) response/recovery curves to 1000 ppm concentration of methane [CH<sub>4</sub>] at 175 °C for ZnO–NR, Pdcat/ZnO–NR, and at 150 °C for T–ZnO and Pdcat/T–ZnO sensors.</p>
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<p>Material properties and schematics of gas sensing mechanisms. Receptor function, transducer function, physicochemical, and material properties of MOS (specifically ZnO) gas sensors listed on the right. The detailed sensing process is shown as a space-charge region model related to surface oxygen ion species describing oxygen adsorption on unsensitized and chemical-electronic sensitized surface with Pd (or Pd–Ag) nanoparticles and band-bending theory. Also shown is a schematic illustrating processes limiting (or enhancing) the kinetics of gas diffusion while inducing surface dipoles, as well as spillover on sensitized ZnO nanorods assembly, nanostructured surface.</p>
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8 pages, 1932 KiB  
Article
High-Harmonic Generation in an Optical Fiber Functionalized with Zinc Oxide Thin Films
by Idris Tiliouine, Yann Leventoux, Jean-Christophe Orlianges, Aurelian Crunteanu, Marie Froidevaux, Hamed Merdji and Sébastien Février
Photonics 2025, 12(1), 82; https://doi.org/10.3390/photonics12010082 - 17 Jan 2025
Viewed by 358
Abstract
High-order harmonic generation (HHG) in semiconductor thin films from ultrashort mid-infrared laser drivers holds the potential for the realization of integrated sources of extreme ultraviolet light. Here, we demonstrate solid-state HHG in zinc oxide thin films synthesized by the radiofrequency reactive magnetron sputtering [...] Read more.
High-order harmonic generation (HHG) in semiconductor thin films from ultrashort mid-infrared laser drivers holds the potential for the realization of integrated sources of extreme ultraviolet light. Here, we demonstrate solid-state HHG in zinc oxide thin films synthesized by the radiofrequency reactive magnetron sputtering process directly on the cleaved facets of optical fibers. Harmonics 3 to 13 of the radiation from a fiber-based laser system delivering 500 kW, 96 fs pulses at 3130 nm are produced in the thin film and guided along the fiber. A proper choice of the laser wavelength and fiber material allows for filtering out the mid-IR pump laser and achieving the HHG mode selection. The possibility to nanostructure the fiber exit by, e.g., focused ion beam milling paves the way to an increased control over the HHG spatial mode. Full article
(This article belongs to the Section Lasers, Light Sources and Sensors)
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Figure 1
<p>Schematic of the set-up used to generate high-order harmonics from a mid-IR fiber laser. CPA: chirped pulse amplifier, HWP: half-wave plate, PBS: polarization beam splitter, L: lens, BPF: bandpass filter. The inset shows a close-up of the ZnO thin film deposited onto the input facet of the fiber. Deep ultraviolet and visible harmonics are generated in the film and guided in the fiber while the silica material absorbs the residual IR light.</p>
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<p>Results of SHG-FROG characterization of the solitonic pulse at the output of the nonlinear fluoride fiber. (<b>a</b>) Measured and (<b>b</b>) retrieved SHG-FROG traces. (<b>c</b>) Spectral profiles retrieved from the SHG-FROG trace (red) and measured with the optical spectrum analyzer (blue). (<b>d</b>) Retrieved temporal intensity and phase profiles.</p>
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<p>X-ray diffractogram of ZnO film deposited at room temperature on a silica substrate. The inset shows a scanning electron micrograph of the ZnO film.</p>
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<p>Measured spectra for (<b>a</b>) the pump laser and (<b>b</b>) the various harmonics. In (<b>b</b>), the dashed line shows the bandgap energy of ZnO (3.37 eV). The harmonic spectra are not corrected for the responsivity of the detector. Harmonics H<sub>11</sub> and H<sub>13</sub> were magnified by a factor of 3 and 30, respectively.</p>
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<p>Intensity scaling of H<sub>7</sub> up to H<sub>13</sub>. The straight lines correspond to the fit function for each harmonic.</p>
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28 pages, 10411 KiB  
Review
Porosity Tunable Metal-Organic Framework (MOF)-Based Composites for Energy Storage Applications: Recent Progress
by Huddad Laeim, Vandana Molahalli, Pongthep Prajongthat, Apichart Pattanaporkratana, Govind Pathak, Busayamas Phettong, Natthawat Hongkarnjanakul and Nattaporn Chattham
Polymers 2025, 17(2), 130; https://doi.org/10.3390/polym17020130 - 8 Jan 2025
Viewed by 645
Abstract
To solve the energy crisis and environmental issues, it is essential to create effective and sustainable energy conversion and storage technologies. Traditional materials for energy conversion and storage however have several drawbacks, such as poor energy density and inadequate efficiency. The advantages of [...] Read more.
To solve the energy crisis and environmental issues, it is essential to create effective and sustainable energy conversion and storage technologies. Traditional materials for energy conversion and storage however have several drawbacks, such as poor energy density and inadequate efficiency. The advantages of MOF-based materials, such as pristine MOFs, also known as porous coordination polymers, MOF composites, and their derivatives, over traditional materials, have been thoroughly investigated. These advantages stem from their high specific surface area, highly adjustable structure, and multifunctional nature. MOFs are promising porous materials for energy storage and conversion technologies, according to research on their many applications. Moreover, MOFs have served as sacrificial materials for the synthesis of different nanostructures for energy applications and as support substrates for metals, metal oxides, semiconductors, and complexes. One of the most intriguing characteristics of MOFs is their porosity, which permits space on the micro- and meso-scales, revealing and limiting their functions. The main goals of MOF research are to create high-porosity MOFs and develop more efficient activation techniques to preserve and access their pore space. This paper examines the porosity tunable mixed and hybrid MOF, pore architecture, physical and chemical properties of tunable MOF, pore conditions, market size of MOF, and the latest development of MOFs as precursors for the synthesis of different nanostructures and their potential uses. Full article
(This article belongs to the Section Polymer Applications)
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Graphical abstract

Graphical abstract
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<p>The development of metal–organic frameworks and their prospects for high-performance supercapacitors [<a href="#B5-polymers-17-00130" class="html-bibr">5</a>].</p>
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<p>The Web of science data of MOF-based material for energy applications (typing keyword MOF, Energy) and number of documents published by type, subject area and the year.</p>
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<p>Utilization of metal–organic frameworks and their derivatives in supercapacitors [<a href="#B10-polymers-17-00130" class="html-bibr">10</a>].</p>
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<p>Development of MOF materials for upcoming generation rechargeable energy sources [<a href="#B14-polymers-17-00130" class="html-bibr">14</a>]. Figure (<b>a</b>) Structure of Ni –MOF, (<b>b</b>) Crystal structure of Ni<sub>3</sub>(HITP)<sub>2</sub>. (<b>c</b>) crystal structure of MOF-199.</p>
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<p>Perfect MOF and covalent organic framework (COF) components for cutting-edge batteries [<a href="#B19-polymers-17-00130" class="html-bibr">19</a>].</p>
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<p>Metal oxide composites produced from MOFs and their potential uses in energy storage [<a href="#B19-polymers-17-00130" class="html-bibr">19</a>].</p>
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<p>Methods for pore architecturing MOFs (<b>a</b>) Structural features and design directions of MOFs. (<b>b</b>–<b>e</b>) General strategies for manipulating pores, including (<b>b</b>) molecular design, (<b>c</b>) templating, (<b>d</b>) controlled assembly, and (<b>e</b>) defect engineering. [<a href="#B22-polymers-17-00130" class="html-bibr">22</a>].</p>
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<p>Strategies for pore architecturing materials generated from MOFs.</p>
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<p>The production of Ni-MOF@PPy and its application in the construction of the asymmetric supercapacitor Ni-MOF@PPy/AC [<a href="#B24-polymers-17-00130" class="html-bibr">24</a>].</p>
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<p>The electrochemical properties of Ni-MOF@PPy//AC ASC are demonstrated by the following: (<b>a</b>) specific capacitance curve at various current densities; (<b>b</b>) CV curves under varying scan rates; (<b>c</b>) GCD curves at various current densities; and (<b>d</b>) CV curves at various voltage windows [<a href="#B23-polymers-17-00130" class="html-bibr">23</a>].</p>
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<p>Substrate materials for high-performance supercapattery devices based on co-MOF and polyaniline. (<b>a</b>). Pictorial illustration of the ASC device, AC//MOF/PANI; CV profiles of AC anode and MOF/PANI cathode (<b>b</b>); GCD curves at various current density (<b>c</b>); specific capacity vs. current density plot (<b>d</b>); specific capacity and columbic efficiency plot (<b>e</b>); and EIS of before stability test, after 3000 GCD cycles and one month later (<b>f</b>) [<a href="#B25-polymers-17-00130" class="html-bibr">25</a>].</p>
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<p>A combination of Ni/Co-MOF-rGO composite as electrode material for high-performance supercapacitors [<a href="#B26-polymers-17-00130" class="html-bibr">26</a>].</p>
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<p>Most commonly employed methods of synthesis of MOFs [<a href="#B30-polymers-17-00130" class="html-bibr">30</a>].</p>
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<p>Schematic pathway of 2D Ni-MOF/C-CNTs [<a href="#B38-polymers-17-00130" class="html-bibr">38</a>].</p>
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<p>Illustration of synthesis process for composite NC/Ni-Ni<sub>3</sub>S<sub>4</sub>/CNTs.</p>
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<p>Modifiable rare-earth fcu-MOFs. An integrated framework to boost CO<sub>2</sub> adsorption energetics and uptake [<a href="#B40-polymers-17-00130" class="html-bibr">40</a>].</p>
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<p>MOFs serve as adaptable carriers for NE encapsulation. NE@MOF composites can be categorized into four groups according to their structural features [<a href="#B43-polymers-17-00130" class="html-bibr">43</a>].</p>
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<p>Pore size contraction-based adsorption kinetics-driven gas/vapor separations using modifiable rare-earth fcu-MOF platform [<a href="#B47-polymers-17-00130" class="html-bibr">47</a>].</p>
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<p>Building MXene @Ce-MOF composites rich in oxygen vacancies for improved energy conversion and storage [<a href="#B48-polymers-17-00130" class="html-bibr">48</a>].</p>
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<p>Composites for structural energy storage that are based on improved carbon fiber electrodes with layered double hydroxide metal–organic frame enhancement [<a href="#B49-polymers-17-00130" class="html-bibr">49</a>].</p>
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<p>An assessment of both redox-active Cu-MOF and Co-MOF as materials for electrodes for hybrid energy storage devices of battery–supercapacitor type [<a href="#B50-polymers-17-00130" class="html-bibr">50</a>].</p>
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<p>Effective use and storage of solar thermal energy based on phase change substances stabilized by MOF@CuO composites [<a href="#B51-polymers-17-00130" class="html-bibr">51</a>].</p>
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<p>Global MOF for marketing field with various applications.</p>
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17 pages, 13090 KiB  
Article
Dynamic Imaging of Projected Electric Potentials of Operando Semiconductor Devices by Time-Resolved Electron Holography
by Tolga Wagner, Hüseyin Çelik, Simon Gaebel, Dirk Berger, Peng-Han Lu, Ines Häusler, Nina Owschimikow, Michael Lehmann, Rafal E. Dunin-Borkowski, Christoph T. Koch and Fariba Hatami
Electronics 2025, 14(1), 199; https://doi.org/10.3390/electronics14010199 - 5 Jan 2025
Viewed by 791
Abstract
Interference gating (iGate) has emerged as a groundbreaking technique for ultrafast time-resolved electron holography in transmission electron microscopy, delivering nanometer spatial and nanosecond temporal resolution with minimal technological overhead. This study employs iGate to dynamically observe the local projected electric potential within the [...] Read more.
Interference gating (iGate) has emerged as a groundbreaking technique for ultrafast time-resolved electron holography in transmission electron microscopy, delivering nanometer spatial and nanosecond temporal resolution with minimal technological overhead. This study employs iGate to dynamically observe the local projected electric potential within the space-charge region of a contacted transmission electron microscopy (TEM) lamella manufactured from a silicon diode during switching between unbiased and reverse-biased conditions, achieving a temporal resolution of 25 ns at a repetition rate of 3 MHz. By synchronizing the holographic acquisition with the applied voltage, this approach enables the direct visualization of time-dependent potential distributions with high precision. Complementary static and dynamic experiments reveal a remarkable correspondence between modeled and measured projected potentials, validating the method’s robustness. The observed dynamic phase progressions resolve and allow one to differentiate between localized switching dynamics and preparation-induced effects, such as charge recombination near the sample edges. These results establish iGate as a transformative tool for operando investigations of semiconductor devices, paving the way for advancing the nanoscale imaging of high-speed electronic processes. Full article
(This article belongs to the Section Optoelectronics)
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<p>Schematic of the time-resolved electron holography setup with interference gating in a transmission electron microscope (TEM). (<b>a</b>) The TEM configuration uses an RF biasing holder to apply a periodic voltage to the sample, creating an electron hologram by overlapping object (Obj) and reference (Ref) waves with a biprism. (<b>b</b>) Holographic reconstruction process: Fourier transformation (FT), isolating sideband (SB) from centerband (CB), extracting amplitude and phase information. (<b>c</b>) Interference Gating: dynamic fringe contrast <math display="inline"><semantics> <msub> <mi>V</mi> <mrow> <mi>h</mi> <mi>o</mi> <mi>l</mi> </mrow> </msub> </semantics></math> with gate length <math display="inline"><semantics> <mi>τ</mi> </semantics></math> (top panel), FT within and outside the gate (second panel), noise-based gating signal applied to dynamic phase shifter (third panel), control signal applied to RF biasing holder (bottom panel), synchronized to each other with an adjustable temporal delay <math display="inline"><semantics> <mrow> <mo>Δ</mo> <mi>t</mi> </mrow> </semantics></math> for setting the gate position <math display="inline"><semantics> <msub> <mi>t</mi> <mi>g</mi> </msub> </semantics></math>.</p>
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<p>(<b>a</b>) Sample preparation and multiscale imaging of the UG1A diode, showcasing the individual steps, ranging from the mechanical preparation to the contacted TEM lamella. The top panel shows a macroscopic view (light microscopy, LM) of the mechanically ground UG1A diode with the device visible, centered in between p- and n-contacts. The middle panel displays a voltage contrast image acquired by Scanning Electron Microscopy (SEM) utilizing a micro-manipulator (colored red) as an electrical contact, indicating a potential difference across the p–n junction interface (plotted in red, from <math display="inline"><semantics> <mrow> <mo>−</mo> <mn>2</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> on the p-side to 0 <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> on the n-side). The bottom panels show SEM images of the FIB-prepared lamella in top (electron image) and side views (ion image), highlighting the p- and n-doped areas within and the vacuum region surrounding the sample. (<b>b</b>) Potential model using SIMP. The upper diagram depicts the initial 2D potential distribution across the p–n junction (red line) and within the supporting chip with an applied reverse-bias <math display="inline"><semantics> <msub> <mi>V</mi> <mrow> <mi>t</mi> <mi>o</mi> <mi>t</mi> </mrow> </msub> </semantics></math>, while the black dashed lines represent the electric potential extending into the vacuum calculated by SIMP. The lower diagram shows a schematic cross-section of the SIMP-based extension of the initial 2D potential with an effective thickness <math display="inline"><semantics> <msub> <mi>t</mi> <mrow> <mi>e</mi> <mi>f</mi> <mi>f</mi> </mrow> </msub> </semantics></math> along the <span class="html-italic">z</span>-axis to the full 3D potential distribution, needed for calculating the projected potentials and simulated phases.</p>
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<p>(<b>a</b>) Normalized simulated phase (calculated by SIMP) of the UG1A diode under reverse-bias condition (<math display="inline"><semantics> <mrow> <msub> <mi>U</mi> <mrow> <mi>e</mi> <mi>x</mi> <mi>t</mi> </mrow> </msub> <mo>=</mo> <mo>−</mo> <mn>2</mn> <mo> </mo> <mi mathvariant="normal">V</mi> </mrow> </semantics></math>). The white boxes indicate the areas used as reference and object wave regions in the static electron holographic experiments and the dashed white box highlight the area of the contacted TEM lamella. (<b>b</b>) Comparison of the modeled phase (difference between object and reference wave regions, top row) with experimental phase reconstructions (bottom row) at different applied biases: <math display="inline"><semantics> <mrow> <msub> <mi>U</mi> <mrow> <mi>e</mi> <mi>x</mi> <mi>t</mi> </mrow> </msub> <mo>=</mo> <mo>−</mo> <mn>2</mn> <mo> </mo> <mi mathvariant="normal">V</mi> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math>, and 0 <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math>. The dashed white boxes highlight the area of the contacted TEM lamella. (<b>c</b>) Phase profiles extracted from SIMP (dotted lines) and experimental data (solid lines) across the diode for varying biasing conditions.</p>
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<p>(<b>a</b>) Static phase reconstruction of the UG1A diode biased with <math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math>, highlighting the space-charge region (SCR) between the p- and n-doped sides. The dashed white box outlines the area of the contacted TEM lamella; the orange polygon outlines the FoV for the time-resolved measurements. (<b>b</b>) Reconstructed dynamic phases, acquired with a time resolution of <math display="inline"><semantics> <mrow> <mi>τ</mi> <mo>=</mo> <mn>25</mn> <mo> </mo> <mi>ns</mi> </mrow> </semantics></math> at a repetition rate of <math display="inline"><semantics> <mrow> <mi>f</mi> <mo>=</mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">MHz</mi> </mrow> </semantics></math>, showing the phase distribution for different switching states (<math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> at <math display="inline"><semantics> <mrow> <mi>t</mi> <mo>=</mo> <mn>150</mn> <mo> </mo> <mi>ns</mi> </mrow> </semantics></math> and 0 <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> at <math display="inline"><semantics> <mrow> <mi>t</mi> <mo>=</mo> <mn>61</mn> <mo> </mo> <mi>ns</mi> </mrow> </semantics></math>) of the diode. The regions marked by orange lines indicate the areas used for the phase profiles in <span class="html-italic">x</span>- and <span class="html-italic">y</span>-directions. (<b>c</b>) Phase profiles at different biases (<math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> and 0 <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math>) with orange dashed lines indicating the spatial range for time-resolved measurements (small FoV), (<b>d</b>) plot of the phase slopes along the <span class="html-italic">x</span>-axis, and (<b>e</b>) phase profiles along the <span class="html-italic">y</span>-axis for <math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> and 0 <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math>.</p>
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<p>(<b>a</b>) Dynamic phase frame of the UG1A diode at <math display="inline"><semantics> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </semantics></math> <math display="inline"><semantics> <mi mathvariant="normal">V</mi> </semantics></math> bias (150 ns), depicting the SCR and its extension into the n-doped region, with the subregions (I–IV) marked for the analysis of the temporal phase progression (in (<b>b</b>)). The lower panel schematically illustrates the position of the equi-phase lines. (<b>b</b>) Normalized phase values over time, averaged in each subregion (I–IV) during diode switching, showing localized phase modulations corresponding to bias changes. The gray-shaded areas indicate the location-dependent transitions captured by iGate. For improved visibility, the period of <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>333.3</mn> <mo> </mo> <mi>ns</mi> </mrow> </semantics></math> is repeated (<math display="inline"><semantics> <mrow> <mi>f</mi> <mo>=</mo> <mn>3</mn> <mo> </mo> <mi>MHz</mi> </mrow> </semantics></math>). (<b>c</b>) Sequential phase frames of the switching behavior into and out of reverse-bias condition, demonstrating the temporal evolution of the equi-phase lines (red dashed) within the SCR.</p>
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13 pages, 2646 KiB  
Article
UV and Visible Light-Induced Photocatalytic Efficiency of Polyaniline/Titanium Dioxide Heterostructures
by Yongqiang Fu and Marcin Janczarek
Molecules 2025, 30(1), 23; https://doi.org/10.3390/molecules30010023 - 25 Dec 2024
Viewed by 511
Abstract
The concept of using polyaniline/titanium dioxide heterostructures as efficient photocatalysts is based on the synergistic effect of conducting polymer and metal oxide semiconductors. Due to inconclusive literature reports, the effect of different polyaniline/TiO2 ratios on photocatalytic activity under UV and visible light [...] Read more.
The concept of using polyaniline/titanium dioxide heterostructures as efficient photocatalysts is based on the synergistic effect of conducting polymer and metal oxide semiconductors. Due to inconclusive literature reports, the effect of different polyaniline/TiO2 ratios on photocatalytic activity under UV and visible light was investigated. In most papers, non-recommended dyes are used as model compounds to evaluate visible light activity. Therefore, colorless phenol was used instead of dyes in this study to clarify the real visible light-induced photocatalytic activity of polyaniline/TiO2 composites. This publication also includes a discussion of whether materials derived from bulk (non-nanostructured) polyaniline and TiO2 by the standard in situ oxidative polymerization method are suitable candidates for promising photocatalytic materials. The evaluation of photocatalytic activity was performed in both UV and visible light systems. X-ray diffraction and UV-Vis diffuse reflectance spectroscopy methods were applied to characterize the obtained samples. Obtained polyaniline (pure and in composites) was identified as emeraldine salt. In the UV system, none of the prepared samples with different polyaniline–titania ratios had activity better than reference P25 titania. It has been observed that the presence of polyaniline adversely affects the photocatalytic properties, as the polyaniline layer covering the titania surface can shield the UV light transmission by blocking the contact between the TiO2 surface and organic molecules. In the case of using visible light, no synergies have been observed between polyaniline and titania either. The photodegradation efficiencies of the most active samples were similar to those of pure polyaniline. In conclusion, in order to obtain efficient polyaniline/titania photocatalysts active in UV and/or visible light, it is necessary to take into account the morphological and surface properties of both components. Full article
(This article belongs to the Special Issue Functional Nanomaterials in Green Chemistry, 2nd Edition)
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<p>The color change of PANI/TiO<sub>2</sub> samples.</p>
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<p>UV-Vis diffuse reflectance spectra of PANI/TiO<sub>2</sub> samples.</p>
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<p>XRD diffractograms of PANI/P25 samples in relation to PANI-ES and P25. A—anatase, R—rutile, and P—polyaniline (emeraldine salt) phases.</p>
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<p>XRD diffractograms of PT1001 sample: before the photocatalytic experiment, after UV, and after visible light-induced experiments.</p>
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<p>UV-induced photodegradation of RhB in the presence of obtained PANI/TiO<sub>2</sub> photocatalysts.</p>
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<p>Calculated RhB photodegradation efficiencies in the UV system for considered PANI-based materials.</p>
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<p>Vis-induced photodegradation of phenol in the presence of obtained PANI/TiO<sub>2</sub> photocatalysts.</p>
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<p>Calculated phenol photodegradation efficiencies in the Vis system for considered PANI-based materials.</p>
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12 pages, 4518 KiB  
Article
Gas Sensor for Efficient Acetone Detection and Application Based on Au-Modified ZnO Porous Nanofoam
by Zhenchao Sun, Shanfu Sun, Xidong Hao, Yinglin Wang, Caili Gong and Pengfei Cheng
Sensors 2024, 24(24), 8100; https://doi.org/10.3390/s24248100 - 19 Dec 2024
Viewed by 542
Abstract
Toxic acetone gas emissions and leakage are a potential threat to the environment and human health. Gas sensors founded on metal oxide semiconductors (MOS) have become an effective strategy for toxic gas detection with their mature process. In the present work, an efficient [...] Read more.
Toxic acetone gas emissions and leakage are a potential threat to the environment and human health. Gas sensors founded on metal oxide semiconductors (MOS) have become an effective strategy for toxic gas detection with their mature process. In the present work, an efficient acetone gas sensor based on Au-modified ZnO porous nanofoam (Au/ZnO) is synthesized by polyvinylpyrrolidone-blowing followed by a calcination method. XRD and XPS spectra were utilized to investigate its structure, while SEM and TEM characterized its morphology. The gas sensitivity of the Au/ZnO sensors was investigated in a static test system. The results reveal that the gas-sensitive performance of porous ZnO toward the acetone can be enhanced by adjusting the loading ratio of noble Au nanoparticles. Specifically, the Au/ZnO sensor prepared by the Au loading ratio of 3.0% (Au/ZnO-3.0%) achieved a 100 ppm acetone gas response of 20.02 at the optimum working temperature of 275 °C. Additionally, a portable electronic device used a STM32 primary control chip to integrate the Au/ZnO-3.0% gas sensor with other modules to achieve the function of detecting and alarming toxic acetone gas. This work is of great significance for efficiently detecting and reducing acetone emissions. Full article
(This article belongs to the Special Issue Advanced Gas Sensors for Toxic Organics Detection)
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<p>XRD patterns of the bare ZnO, Au/ZnO-0.5%, Au/ZnO-1.0%, Au/ZnO-3.0%, and Au/ZnO-5.0% samples.</p>
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<p>SEM images of the as-synthesized sensitive materials: (<b>a</b>,<b>b</b>) bare ZnO; (<b>c</b>) Au/ZnO-0.5%; (<b>d</b>) Au/ZnO-1.0%; (<b>e</b>) Au/ZnO-3.0%; and (<b>f</b>) Au/ZnO-5.0%.</p>
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<p>(<b>a</b>,<b>b</b>) TEM images; (<b>c</b>) HRTEM image; (<b>d</b>) EDX spectrum; and (<b>e</b>) high-angle annular dark-field TEM (HAADF-TEM) and EDX elements mappings of the Au/ZnO-3.0% sample.</p>
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<p>XPS spectra of Au/ZnO-3.0% and pure ZnO sensitive material: (<b>a</b>) XPS survey spectrum; (<b>b</b>) O 1s; (<b>c</b>) Zn 2P; and (<b>d</b>) Au 4f.</p>
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<p>The gas-sensing properties of ZnO, Au/ZnO-0.5%, Au/ZnO-1.0%, Au/ZnO-3.0%, and Au/ZnO-5.0% to 100 ppm acetone: (<b>a</b>) Response to 100 ppm acetone at 200–300 °C; (<b>b</b>) responses to 100 ppm various target gases at 275 °C; and (<b>c</b>) response and recovery time of the Au/ZnO-3.0% sensor to 100 ppm acetone at 275 °C.</p>
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<p>(<b>a</b>) Reversible cycles of Au/ZnO−3.0% to 100 ppm acetone at 275 °C; (<b>b</b>) the concentration gradient dynamic response curve of Au/ZnO−3.0% to 10−150 ppm acetone at 275 °C; and (<b>c</b>) the corresponding linear fit curve.</p>
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<p>Typical signal output circuit of Au/ZnO-3.0% gas sensor in the acetone-detecting device.</p>
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<p>(<b>a</b>,<b>b</b>) Acetone-detecting device design; and (<b>c</b>–<b>f</b>) its display in acetone-detecting process.</p>
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17 pages, 6521 KiB  
Article
Rational Fabrication of Ag2S/g-C3N4 Heterojunction for Photocatalytic Degradation of Rhodamine B Dye Under Natural Solar Radiation
by Ali Alsalme, Ahmed Najm, Nagy N. Mohammed, M. F. Abdel Messih, Ayman Sultan and Mohamed Abdelhay Ahmed
Catalysts 2024, 14(12), 914; https://doi.org/10.3390/catal14120914 - 11 Dec 2024
Viewed by 847
Abstract
Near-infrared light-triggered photocatalytic water treatment has attracted significant attention in recent years. In this novel research, rational sonochemical fabrication of Ag2S/g-C3N4 nanocomposites with various compositions of Ag2S (0–25) wt% was carried out to eliminate hazardous rhodamine [...] Read more.
Near-infrared light-triggered photocatalytic water treatment has attracted significant attention in recent years. In this novel research, rational sonochemical fabrication of Ag2S/g-C3N4 nanocomposites with various compositions of Ag2S (0–25) wt% was carried out to eliminate hazardous rhodamine B dye in a cationic organic pollutant model. g-C3N4 sheets were synthesized via controlled thermal annealing of microcrystalline urea. However, black Ag2S nanoparticles were synthesized through a precipitation-assisted sonochemical route. The chemical interactions between various compositions of Ag2S and g-C3N4 were carried out in an ultrasonic bath with a power of 300 W. XRD, PL, DRS, SEM, HRTEM, mapping, BET, and SAED analysis were used to estimate the crystalline, optical, nanostructure, and textural properties of the solid specimens. The coexistence of the diffraction peaks of g-C3N4 and Ag2S implied the successful production of Ag2S/g-C3N4 heterojunctions. The band gap energy of g-C3N4 was exceptionally reduced from 2.81 to 1.5 eV with the introduction of 25 wt% of Ag2S nanoparticles, implying the strong absorbability of the nanocomposites to natural solar radiation. The PL signal intensity of Ag2S/g-C3N4 was reduced by 40% compared with pristine g-C3N4, implying that Ag2S enhanced the electron–hole transportation and separation. The rate of the photocatalytic degradation of rhodamine B molecules was gradually increased with the introduction of Ag2S on the g-C3N4 surface and reached a maximum for nanocomposites containing 25 wt% Ag2S. The radical trapping experiments demonstrated the principal importance of reactive oxygen species and hot holes in destroying rhodamine B under natural solar radiation. The charge transportation between Ag2S and g-C3N4 semiconductors proceeded through the type I straddling scheme. The enriched photocatalytic activity of Ag2S/g-C3N4 nanocomposites resulted from an exceptional reduction in band gap energy and controlling the electron–hole separation rate with the introduction of Ag2S as an efficient photothermal photocatalyst. The novel as-synthesized nanocomposites are considered a promising photocatalyst for destroying various types of organic pollutants under low-cost sunlight radiation. Full article
(This article belongs to the Section Photocatalysis)
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<p>XRD of g-C<sub>3</sub>N<sub>4</sub>, Ag<sub>2</sub>S, and CNAgS25 nanocomposites.</p>
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<p>N<sub>2</sub>-adsorption isotherm of (<b>a</b>) g-C<sub>3</sub>N<sub>4</sub> and (<b>b</b>) CNAgS25.</p>
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<p>(<b>a</b>) SEM of CNAgS25, (<b>b</b>) mapping of CNAgS25, (<b>c</b>) mapping of C, (<b>d</b>) mapping of (N), (<b>e</b>) mapping of Ag, (<b>f</b>) mapping of S, (<b>g</b>) EDX of CNAgS25.</p>
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<p>(<b>a</b>) TEM of CNAgS25, (<b>b</b>) HRTEM of CNAgS25 and (<b>c</b>) SAED of CNAgS25.</p>
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<p>(<b>a</b>) TEM of CNAgS25, (<b>b</b>) HRTEM of CNAgS25 and (<b>c</b>) SAED of CNAgS25.</p>
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<p>(<b>a</b>) DRS of g-C<sub>3</sub>N<sub>4</sub>, Ag<sub>2</sub>S, CNAgS15, and CNAgS25. (<b>b</b>) Tauc plot of g-C<sub>3</sub>N<sub>4</sub>, Ag2S, CNAgS15, and CNAgS25.</p>
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<p>PL analysis of g-C<sub>3</sub>N<sub>4</sub>, NAgS15, and CNAgS25.</p>
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<p>The absorption spectrum for photocatalytic degradation of rhodamine B over the surfaces of g-C3N4, CNAg10, CNAg15, and CNAg25.</p>
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<p>(<b>a</b>) The variations in the amount of RhB removed (%) under dark and light reactions with the illumination time over the surfaces of g-C<sub>3</sub>N<sub>4</sub>, CNAg10, CNAg15, and CNAg25. (<b>b</b>) The kinetic first-order plot for photocatalytic degradation of RhB dye over the surfaces of g-C<sub>3</sub>N<sub>4</sub>, CNAg10, CNAg15, and CNAg25.</p>
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<p>Photocatalytic degradation of rhodamine B (2 × 10<sup>−5</sup> M) over CNAgS25 nanocomposite in the presence of 2 × 10<sup>−5</sup> M of the following scavengers: (<b>a</b>) benzoquinone, (<b>b</b>) ammonium oxalate, and (<b>c</b>) isopropanol. (<b>d</b>) PL spectrum of terephthalic acid 2 × 10<sup>−4</sup> M over CNAgS25 nanocomposite at 325 nm excitation wavelength.</p>
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<p>Photocatalytic degradation of rhodamine B (2 × 10<sup>−5</sup> M) over CNAgS25 nanocomposite in the presence of 2 × 10<sup>−5</sup> M of the following scavengers: (<b>a</b>) benzoquinone, (<b>b</b>) ammonium oxalate, and (<b>c</b>) isopropanol. (<b>d</b>) PL spectrum of terephthalic acid 2 × 10<sup>−4</sup> M over CNAgS25 nanocomposite at 325 nm excitation wavelength.</p>
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<p>Regeneration of CNAgS25 for five consecutive cycles for removal of RhB dye over CNAgS25 nanocomposite.</p>
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<p>A scheme for electron transportation between g-C<sub>3</sub>N<sub>4</sub> and Ag<sub>2</sub>S semiconductors.</p>
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<p>Scheme for synthesis of (<b>a</b>) g-C<sub>3</sub>N<sub>4</sub>, (<b>b</b>) Ag<sub>2</sub>S and (<b>c</b>) Ag<sub>2</sub>S/g-C<sub>3</sub>N<sub>4</sub> heterojunction.</p>
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22 pages, 42938 KiB  
Article
Electronic and Optical Properties of One-Dimensional Van Der Waals Nanodevices Based on MoS2(n,n) and MoSe2(n,n) Nanotubes
by Daulet Sergeyev, Ainur Duisenova and Kuanyshbek Shunkeyev
Crystals 2024, 14(12), 1055; https://doi.org/10.3390/cryst14121055 - 5 Dec 2024
Viewed by 941
Abstract
In this work, the optical and electronic characteristics of MoS2(n,n) and MoSe2(n,n) nanotubes and 1D van der Waals nanoheterostructures based on them are determined from first principles. It is shown that with an increase in the diameters of MoS [...] Read more.
In this work, the optical and electronic characteristics of MoS2(n,n) and MoSe2(n,n) nanotubes and 1D van der Waals nanoheterostructures based on them are determined from first principles. It is shown that with an increase in the diameters of MoS2(n,n) and MoSe2(n,n) nanotubes, their bandgaps increase (in MoS2(n,n), the gap varies from 0.27 eV to 1.321 eV, and in MoSe2(n,n) from 0.153 eV to 1.216 eV). It was found that with an increase in the diameter of the nanotubes, the static permittivity decreases; van der Waals nanostructures of MoS2(8,8)@MoSe2(16,16) and MoS2(6,6)@MoSe2(14,14) consisting of coaxially compound MoS2(8,8) and MoSe2(16,16), MoS2(6,6) and MoSe2(14,14), respectively, have high static dielectric permittivitiesof 6. 5367 and 3.0756. Such nanoheterostructures offer potential for developing various nanoelectronic devices due to the possibility of effective interaction with an electric field. Studies revealed that the van der Waals nanostructures MoSe2(6,6)@MoS2(14,14) and MoSe2(8,8)@MoS2(16,16) exhibit a semiconductor nature with bandgap widths of 0.174 eV and 0.53 eV, respectively, and MoS2(6,6)@MoSe2(14,14) and MoS2(8,8)@MoSe2(16,16) exhibit metallic properties. Stepped areas of Coulomb origin with a constant period at a voltage of 0.448 V appear on the current–voltage characteristic of the van der Waals nanoheterodevices. It is found that MoSe2(6,6)@MoS2(14,14) and MoSe2(8,8)@MoS2(16,16) nanodevices transmit electric current preferentially in the forward direction due to the formation of a nanoheterojunction between semiconductor nanotubes with different forbidden band values. The fundamental regularities obtained during the study can be useful for the further development of electronic components of nano- and microelectronics. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
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<p>Geometry of MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16) nanodevices.</p>
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<p>Geometry of MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16)nanodevices.</p>
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<p>Geometry of MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14)nanodevices.</p>
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<p>Geometry of MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14)nanodevices.</p>
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<p>Electronic zone structure of MoS<sub>2</sub>(n,m) nanotubes: (<b>a</b>) MoS<sub>2</sub>(6,6); (<b>b</b>) MoS<sub>2</sub>(8,8); (<b>c</b>) MoS<sub>2</sub>(10,10); (<b>d</b>) MoS<sub>2</sub>(12,12); (<b>e</b>) MoS<sub>2</sub>(14,14); (<b>f</b>) MoS<sub>2</sub>(16,16).</p>
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<p>Electronic zone structure of MoS<sub>2</sub>(n,m) nanotubes: (<b>a</b>) MoS<sub>2</sub>(6,6); (<b>b</b>) MoS<sub>2</sub>(8,8); (<b>c</b>) MoS<sub>2</sub>(10,10); (<b>d</b>) MoS<sub>2</sub>(12,12); (<b>e</b>) MoS<sub>2</sub>(14,14); (<b>f</b>) MoS<sub>2</sub>(16,16).</p>
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<p>Electronic zone structure of MoSe<sub>2</sub>(n,m) nanotubes: (<b>a</b>) MoSe<sub>2</sub>(6,6); (<b>b</b>) MoSe<sub>2</sub>(8,8); (<b>c</b>) MoSe<sub>2</sub>(10,10); (<b>d</b>) MoSe<sub>2</sub>(12,12); (<b>e</b>) MoSe<sub>2</sub>(14,14); (<b>f</b>) MoSe<sub>2</sub>(16,16).</p>
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<p>Electronic zone structure of MoSe<sub>2</sub>(n,m) nanotubes: (<b>a</b>) MoSe<sub>2</sub>(6,6); (<b>b</b>) MoSe<sub>2</sub>(8,8); (<b>c</b>) MoSe<sub>2</sub>(10,10); (<b>d</b>) MoSe<sub>2</sub>(12,12); (<b>e</b>) MoSe<sub>2</sub>(14,14); (<b>f</b>) MoSe<sub>2</sub>(16,16).</p>
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<p>Dependence of the complex dielectric constant of MoS<sub>2</sub>(n,n) nanotubes: (<b>a</b>) real part; (<b>b</b>) imaginary part.</p>
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<p>Dependence of the complex dielectric constant of MoSe<sub>2</sub>(n,n) nanotubes: (<b>a</b>) real part; (<b>b</b>) imaginary part.</p>
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<p>Optical characteristics of MoS<sub>2</sub>(n,n) nanotubes: (<b>a</b>) energy dependence of the absorption coefficient; (<b>b</b>) energy dependence of the refractive index.</p>
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<p>Optical characteristics of MoSe<sub>2</sub>(n,n) nanotubes: (<b>a</b>) energy dependence of the absorption coefficient; (<b>b</b>) energy dependence of the refractive index.</p>
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<p>Electronic zone structure of van der Waals nanotubes: (<b>a</b>) MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14); (<b>b</b>) MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14); (<b>c</b>) MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16); (<b>d</b>) MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16).</p>
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<p>Dependence of the complex permittivity of one-dimensional nanodevices MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14); MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14); MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16); MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16): (<b>a</b>) real part; (<b>b</b>) imaginary part.</p>
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<p>Optical characterizations of one-dimensional MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14); MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14); MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16); MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16) nanodevices: (<b>a</b>) energy dependence of the absorption coefficient; (<b>b</b>) energy dependence of the refractive index.</p>
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<p>Current–voltage characteristics of van der Waals nanotubes MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14); MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14); MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16); MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16).</p>
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<p>dI/dV spectra of van der Waals nanotubes MoS<sub>2</sub>(6,6)@MoSe<sub>2</sub>(14,14); MoSe<sub>2</sub>(6,6)@MoS<sub>2</sub>(14,14); MoS<sub>2</sub>(8,8)@MoSe<sub>2</sub>(16,16); MoSe<sub>2</sub>(8,8)@MoS<sub>2</sub>(16,16).</p>
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<p>Geometry of MoS<sub>2</sub>(6,6), MoS<sub>2</sub>(8,8), MoS<sub>2</sub>(14,14), and MoS<sub>2</sub>(16,16) nanotubes.</p>
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<p>Geometry of MoS<sub>2</sub>(6,6), MoS<sub>2</sub>(8,8), MoS<sub>2</sub>(14,14), and MoS<sub>2</sub>(16,16) nanotubes.</p>
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<p>Geometry of MoSe<sub>2</sub>(6,6), MoSe<sub>2</sub>(8,8), MoSe<sub>2</sub>(14,14), and MoSe<sub>2</sub>(16,16) nanotubes.</p>
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<p>Geometry of MoSe<sub>2</sub>(6,6), MoSe<sub>2</sub>(8,8), MoSe<sub>2</sub>(14,14), and MoSe<sub>2</sub>(16,16) nanotubes.</p>
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<p>Electronic zone structure of MoS<sub>2</sub>(n,0): (<b>a</b>) MoS<sub>2</sub>(10,0), (<b>b</b>) MoSe<sub>2</sub>(12,0), (<b>c</b>) MoS<sub>2</sub>(14,0).</p>
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<p>Electronic zone structure of MoSe<sub>2</sub>(n,0): (<b>a</b>) MoSe<sub>2</sub>(10,0), (<b>b</b>) MoSe<sub>2</sub>(12,0), (<b>c</b>) MoSe<sub>2</sub>(14,0).</p>
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9 pages, 1882 KiB  
Article
A PDMS-Al Triboelectric Nanogenerator Using Two-Pulse Laser to Enhance Effective Contact Area and Its Application
by You-Jun Huang, Chi-Hung Tsai, Chia-Wei Hung and Chen-Kuei Chung
Polymers 2024, 16(23), 3397; https://doi.org/10.3390/polym16233397 - 2 Dec 2024
Viewed by 574
Abstract
A triboelectric nanogenerator (TENG) is a kind of energy harvester which converts mechanical energy into electrical energy with electron transfer and transport between two different materials during cycling tribology. To increase the contact area between tribo-layers and enhance the output of TENGs, many [...] Read more.
A triboelectric nanogenerator (TENG) is a kind of energy harvester which converts mechanical energy into electrical energy with electron transfer and transport between two different materials during cycling tribology. To increase the contact area between tribo-layers and enhance the output of TENGs, many studies prepare patterned micro/nanostructured tribo-layers using semiconductor processes like lithography and etching at high cost and with long processing times. Here, we propose a new method to quickly produce high-aspect-ratio (HAR) microneedles of polydimethylsiloxane (PDMS) for TENG triboelectric layers using a two-pulse laser-ablated polymethyl methacrylate mold and casting. It has the merit of employing low-cost CO2 laser microfabrication and polymer casting in a feasible way to produce efficient tribo-electric layers. Two-pulse laser ablation is an efficient method for fabricating HAR microstructures with increasing depth at a constant width and density compared to single-pulse ablation. It enhances the depth of microneedles at a constant width and successfully casts PDMS tribo-layers with microneedles that have an aspect ratio 1.88 times higher than those produced by the traditional single-pulse process. The microneedle-PDMS (MN-PDMS) layer is combined with Al sheets to form the MN-PDMS-Al TENG. Compared with the flat PDMS-Al TENG and single-pulse PDMS-Al TENG, the two-pulse TENG enhances open-circuit voltage (Voc) by 1.63 and 1.48 times, the short-circuit current (Isc) by 1.92 and 1.47 times, and the output power by 3.69 and 2.16 times, respectively. This two-pulse ablation method promotes the output performance of TENGs, which has the potential for applications in self-powered devices and sustainable energy. Full article
(This article belongs to the Special Issue Polymer Micro/Nanofabrication and Manufacturing II)
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<p>Two types of PDMS microneedle structures processed via laser were captured through OM imaging: (<b>a</b>) The SPL-PDMS tribo-layer, produced with a single laser pass, shows a height of 320 μm and a surface area of 3369 mm<sup>2</sup> at a width of 220 μm; (<b>b</b>) the TPL-PDMS tribo-layer, produced with a double laser pass, achieves a height of 600 μm (1.88 times greater) and a surface area of 4308 mm<sup>2</sup> (1.28 times greater) at the same width.</p>
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<p>Output signal differences among the three TENG types: (<b>a</b>) the Voc for the flat PDMS-Al TENG, SPL PDMS-Al TENG, and TPL PDMS-Al TENG are 54.2 V, 59.7 V, and 88.4 V, respectively; (<b>b</b>) the Isc for the flat PDMS-Al TENG, SPL PDMS-Al TENG, and TPL PDMS-Al TENG are 26.5 μA, 34.5 μA, and 50.9 μA, respectively. It can be observed that the TPL PDMS-Al TENG shows a significant enhancement in both Voc and Isc compared to the flat PDMS-Al TENG and SPL PDMS-Al TENG.</p>
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<p>Output waveform of TPL-PDMS TENG during continuous operation on a pneumatic cylinder actuation platform for 1000 times, demonstrating that the output voltage remains stable without significant variation.</p>
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<p>Number of LEDs driven by different PDMS TENGs: (<b>a</b>) TPL-PDMS TENG driving 500 LEDs, (<b>b</b>) SPL-PDMS TENG driving 300 LEDs, (<b>c</b>) flat PDMS TENG driving 270 LEDs.</p>
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<p>When the TPL-PDMS tribo-layer is used as a biomechanical sensor, it captures wrist flexion and extension signals. (<b>a</b>) When the subject’s wrist is extended, the TPL-PDMS tribo-layer separates from the skin, as shown in the red-circled area; (<b>b</b>) when the wrist flexes, the TPL-PDMS tribo-layer contacts the skin, as shown in the red-circled area, completing the contact–separation cycle; (<b>c</b>) voltage output graph of wrist flexion and extension detected by the TPL-PDMS tribo-layer, generating a peak signal of up to 1.34 V.</p>
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<p>When the TPL-PDMS tribo-layer is used as a biomechanical sensor, it captures elbow flexion and extension signals. (<b>a</b>) When the subject’s elbow is extended, the TPL-PDMS tribo-layer separates from the skin, as shown in the red-circled area; (<b>b</b>) when the elbow is flexed, the TPL-PDMS tribo-layer contacts the skin, as shown in the red-circled area, completing the contact–separation cycle; (<b>c</b>) voltage output graph of elbow flexion and extension detected by the TPL-PDMS tribo-layer, generating a peak signal of up to 4.56 V.</p>
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14 pages, 3443 KiB  
Article
Menthol-Induced Chirality in Semiconductor Nanostructures: Chiroptical Properties of Atomically Thin 2D CdSe Nanoplatelets Capped with Enantiomeric L-(−)/D-(+)-Menthyl Thioglycolates
by Maria Yu. Skrypnik, Daria A. Kurtina, Sofia P. Karamysheva, Evgeniia A. Stepanidenko, Irina S. Vasil’eva, Shuai Chang, Alexander I. Lebedev and Roman B. Vasiliev
Nanomaterials 2024, 14(23), 1921; https://doi.org/10.3390/nano14231921 - 28 Nov 2024
Cited by 1 | Viewed by 923
Abstract
Semiconductor colloidal nanostructures capped with chiral organic molecules are a research hotspot due to their wide range of important implications for photonic and spintronic applications. However, to date, the study of chiral ligands has been limited almost exclusively to naturally occurring chiral amino [...] Read more.
Semiconductor colloidal nanostructures capped with chiral organic molecules are a research hotspot due to their wide range of important implications for photonic and spintronic applications. However, to date, the study of chiral ligands has been limited almost exclusively to naturally occurring chiral amino and hydroxy acids, which typically contain only one stereocenter. Here, we show the pronounced induction of chirality in atomically thin CdSe nanoplatelets (NPLs) by capping them with enantiopure menthol derivatives as multi-stereocenter molecules. L-(−)/D-(+)-menthyl thioglycolate, easily synthesized from L-(−)/D-(+)-menthol, is attached to Cd-rich (001) basal planes of 2- and 3-monolayer (ML) CdSe NPLs. We show the appearance of narrow sign-alternating bands in the circular dichroism (CD) spectra of 2 ML NPLs corresponding to heavy-hole (HH) and light-hole (LH) excitons with maximal dissymmetry g-factor up to 2.5 × 10−4. The most intense CD bands correspond to the lower-energy HH exciton, and in comparison with the N-acetyl-L-Cysteine ligand, the CD bands for L-(−)-menthyl thioglycolate have the opposite sign. The CD measurements are complemented with magnetic CD measurements and first-principles modeling. The obtained results may be of interest for designing new chiral semiconductor nanostructures and improving understanding of their chiroptical properties. Full article
(This article belongs to the Special Issue Nano Surface Engineering)
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<p>(<b>a</b>) Scheme of synthesis of chiral ester from menthol and thioglycolic acid. (<b>b</b>) Structural formulas of mirror stereoisomers of L-(−)/D-(+)-menthyl thioglycolate. (<b>c</b>) Scheme of attachment of chiral ester to basal planes of CdSe nanoplatelets due to formation of cadmium–sulfur bond. Note the nonpolar outer surface of the obtained nanoplatelets, caused by cyclohexane fragments of the ester.</p>
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<p>(<b>a</b>) FTIR spectra of the initial reagents, TGA (green line) and L-menthol (grey line), and spectrum of the synthesized ester menthylTG sample (blue line). (<b>b</b>) FTIR spectra of menthylTG-capped CdSe2ML_menthylTG (blue line) sample. Black line shows the FTIR spectrum of the initial OA-capped CdSe2ML_OA sample. Positions of the main vibration bands are marked by black vertical lines. The spectra are offset for clarity. Typical absorbance spectra of (<b>c</b>) CdSe2ML_OA NPLs (black solid line) and (<b>d</b>) the same sample after ligand exchange with menthylTG (CdSe2ML_menthylTG, blue line) and thioglycolic acid (CdSe2ML_TGA, green line) ligands. (<b>e</b>) Modification of absorbance spectra during the ligand exchange at different times. Black arrows show changes in the intensity of bands during the ligand exchange.</p>
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<p>TEM images of the transformation of as-synthesized scroll-like CdSe2ML_OA NPLs covered with oleic acid ligands (<b>a</b>) to flat CdSe2ML_menthylTG NPLs after ligand exchange with L-menthylTG (<b>b</b>). Insets: enlarged images of NPL ensembles.</p>
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<p>(<b>a</b>) CD spectra of 2 ML CdSe NPLs coated with L-(−)-menthyl thioglycolate (blue line), D-(+)-menthyl thioglycolate (red line), and achiral TGA ligands (grey line). (<b>b</b>) Comparison of CD spectra of CdSe3ML_L-MenthyTG (green line) and CdSe2ML_L-MenthyTG (blue line) samples emphasizing the effect of thickness. The CD spectrum of free L-MenthyTG (black line) is shown for comparison. (<b>c</b>) Decomposition of the CD spectrum of 2 ML CdSe NPLs coated with L-(−)-menthyl thioglycolate into the sum of Lorentz lines. Empty circles are experimental data, dashed green lines are Lorentz profiles, and the red line is the sum of Lorentz profiles. (<b>d</b>) Comparison of CD spectra of 2 ML CdSe NPLs coated with L-(−)-menthyl thioglycolate (blue line) and L-acetylcysteine (red line). All panels show the corresponding absorption spectra at the top.</p>
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<p>DFT models of the crystal structure of 2 ML CdSe NPLs coated with (<b>a</b>) L-(−)-menthyl thioglycolate, in a [110] orientation, (<b>b</b>) L-(−)-menthyl thioglycolate, in a [001] orientation, and (<b>c</b>) thioglycolic acid, in [110] orientation. Atoms are marked: Cd—green, Se—purple, S—yellow, O—red.</p>
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<p>MCD spectra of 2 ML CdSe NPL samples coated with (<b>a</b>) L-(−)-menthyl thioglycolate and (<b>b</b>) TGA ligands. The spectra were recorded from NPL dispersions in (<b>a</b>) THF and (<b>b</b>) methanol. The measurements were performed in magnetic fields up to ±1.5 T. The spectra were recorded with an interval of 0.5 T.</p>
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37 pages, 8367 KiB  
Review
Advances in Surface-Enhanced Raman Spectroscopy for Urinary Metabolite Analysis: Exploiting Noble Metal Nanohybrids
by Ningbin Zhao, Peizheng Shi, Zengxian Wang, Zhuang Sun, Kaiqiang Sun, Chen Ye, Li Fu and Cheng-Te Lin
Biosensors 2024, 14(12), 564; https://doi.org/10.3390/bios14120564 - 21 Nov 2024
Viewed by 751
Abstract
This review examines recent advances in surface-enhanced Raman spectroscopy (SERS) for urinary metabolite analysis, focusing on the development and application of noble metal nanohybrids. We explore the diverse range of hybrid materials, including carbon-based, metal–organic-framework (MOF), silicon-based, semiconductor, and polymer-based systems, which have [...] Read more.
This review examines recent advances in surface-enhanced Raman spectroscopy (SERS) for urinary metabolite analysis, focusing on the development and application of noble metal nanohybrids. We explore the diverse range of hybrid materials, including carbon-based, metal–organic-framework (MOF), silicon-based, semiconductor, and polymer-based systems, which have significantly improved SERS performance for detecting key urinary biomarkers. The principles underlying SERS enhancement in these nanohybrids are discussed, elucidating both electromagnetic and chemical enhancement mechanisms. We analyze various fabrication methods that enable precise control over nanostructure morphology, composition, and surface chemistry. The review critically evaluates the analytical performance of different hybrid systems for detecting specific urinary metabolites, considering factors such as sensitivity, selectivity, and stability. We address the analytical challenges associated with SERS-based urinary metabolite analysis, including sample preparation, matrix effects, and data interpretation. Innovative solutions, such as the integration of SERS with microfluidic devices and the application of machine learning algorithms for spectral analysis, are highlighted. The potential of these advanced SERS platforms for point-of-care diagnostics and personalized medicine is discussed, along with future perspectives on wearable SERS sensors and multi-modal analysis techniques. This comprehensive overview provides insights into the current state and future directions of SERS technology for urinary metabolite detection, emphasizing its potential to revolutionize non-invasive health monitoring and disease diagnosis. Full article
(This article belongs to the Special Issue Feature Paper in Biosensor and Bioelectronic Devices 2024)
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<p>Schematic diagram of EM (<b>A</b>) and CM (<b>B</b>).</p>
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<p>TEM images of monodispersed gold nanostars (<b>A</b>), gold nanorods (<b>B</b>), gold nano-bipyramids (<b>C</b>), spherical gold nanoparticles (<b>D</b>), gold nanocubes (<b>E</b>), and gold nanotriangles (<b>F</b>). Reprinted with permission from refs. [<a href="#B28-biosensors-14-00564" class="html-bibr">28</a>,<a href="#B29-biosensors-14-00564" class="html-bibr">29</a>,<a href="#B30-biosensors-14-00564" class="html-bibr">30</a>,<a href="#B31-biosensors-14-00564" class="html-bibr">31</a>,<a href="#B32-biosensors-14-00564" class="html-bibr">32</a>]. Copyright Elsevier and ACS.</p>
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<p>Correlation of SERS intensity and scattering resonance. Gold nanoparticle faceting and impact on SERS enhancement. Reprinted with permission from ref. [<a href="#B35-biosensors-14-00564" class="html-bibr">35</a>]. Copyright 2016 ACS.</p>
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<p>AFM images of the surface of Ag substrate before and after irradiating by femtosecond laser. Reprinted with permission from ref. [<a href="#B44-biosensors-14-00564" class="html-bibr">44</a>]. Copyright 2011 Elsevier.</p>
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<p>SEM image of the created Si nanopillars and the AgNPs formed on the Si nanopillars. Reprinted with permission from ref. [<a href="#B51-biosensors-14-00564" class="html-bibr">51</a>]. Copyright 2017 ACS.</p>
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<p>Synthetic route for antibody-modified Fe<sub>3</sub>O<sub>4</sub>@Ag magnetic tags and schematic diagram of the magnetic SERS Strip for detecting two respiratory viruses. Reprinted with permission from ref. [<a href="#B52-biosensors-14-00564" class="html-bibr">52</a>]. Copyright 2019 ACS.</p>
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<p>Schematic representation of Au@MIP fabrication process. Reprinted with permission from ref. [<a href="#B53-biosensors-14-00564" class="html-bibr">53</a>]. Copyright 2020 ACS.</p>
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<p>Energy-level diagrams illustrating the electronic transitions. The calculated band structures of MoS<sub>2</sub> a and MoS<sub>x</sub>O<sub>y</sub> taking Fermi level as the reference. Schematic energy-level diagrams of R6G on c MoS<sub>x</sub>O<sub>y</sub> and d MoS<sub>2</sub> and MoO<sub>3</sub> with respect to the vacuum level. Reprinted with permission from ref. [<a href="#B56-biosensors-14-00564" class="html-bibr">56</a>]. Copyright 2017 Nature.</p>
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<p>The proposed mechanisms of the CT process in the Ag–rGO system and SiO<sub>2</sub>–Ag–rGO system combined with 4-MBA molecules. Reprinted with permission from ref. [<a href="#B62-biosensors-14-00564" class="html-bibr">62</a>]. Copyright 2021 ACS.</p>
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<p>Schematic illustration of the one-pot synthesis of AuNPLs on CNT sheet (<b>A</b>) and the synthetic procedure of Au/AgNP/crossed CNT substrate (<b>B</b>). Reprinted with permission from refs. [<a href="#B66-biosensors-14-00564" class="html-bibr">66</a>,<a href="#B67-biosensors-14-00564" class="html-bibr">67</a>]. Copyright 2017 ACS and 2021 MDPI.</p>
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<p>Illustration of the preparation of 2D Ni-MOF-Au@AgNPs composite. Reprinted with permission from ref. [<a href="#B73-biosensors-14-00564" class="html-bibr">73</a>]. Copyright 2022 Elsevier.</p>
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<p>Optical image of the Ag/pSi SERS substrate (<b>a</b>) and SERS mapping (<b>b</b>) for 10<sup>−5</sup> M R6G on the area (<b>A</b>). Schematics of the Galvanic replacement reaction of silver dendritic nanoforests on silicon (Ag-DNFs/Si) (<b>B</b>). Reprinted with permission from refs. [<a href="#B76-biosensors-14-00564" class="html-bibr">76</a>,<a href="#B78-biosensors-14-00564" class="html-bibr">78</a>]. Copyright 2019 Elsevier and 2020 MDPI.</p>
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<p>Top-view FESEM images for TiO2-NTFs exposed for different times to UVC radiation: 5 (<b>a</b>), 15 (<b>b</b>), 30 (<b>c</b>) and 60 min (<b>d</b>); with pre-immersion treatment in 50 mM AgNO<sub>3</sub> (<b>A</b>). Schematic diagram for the synthesis of HGNs and HGNs-MBA@ZnS with well-controlled core morphology and tshell (<b>B</b>). Reprinted with permission from ref. [<a href="#B80-biosensors-14-00564" class="html-bibr">80</a>,<a href="#B81-biosensors-14-00564" class="html-bibr">81</a>]. Copyright 2024 Elsevier.</p>
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<p>The schematic representation showing the fabrication of polymer/Ag core-shell microspheres and SERS application (<b>A</b>). Schematic diagram of the fabrication SERS-active substrate. (<b>B</b>): preparation of AuNPLs capture probe (<b>I</b>), preparation of PLA fiber flexible substrate (<b>II</b>), preparation of SERS nanotags (<b>III</b>). Reprinted with permission from refs. [<a href="#B85-biosensors-14-00564" class="html-bibr">85</a>,<a href="#B86-biosensors-14-00564" class="html-bibr">86</a>]. Copyright 2022 Elsevier and 2024 Elsevier.</p>
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<p>Schematic diagrams of AgNPs@mrGO SERS-active substrate. Reprinted with permission from ref. [<a href="#B90-biosensors-14-00564" class="html-bibr">90</a>]. Copyright 2020 Elsevier.</p>
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<p>Principle of AuCOF preparation and aptamer-regulated AuCOF catalyzed RRS/SERS coupled dual-mode assay for small molecule (<b>A</b>). Synthesis of bovine serum albumin (BSA)-modified silver nanoparticles capped with 4-mercaptopyridine (AgNP-MPy), microcapsules containing BSA-modified MPy-AgNPs, and the urea sensing hydrogel (<b>B</b>). Reprinted with permission from refs. [<a href="#B100-biosensors-14-00564" class="html-bibr">100</a>,<a href="#B103-biosensors-14-00564" class="html-bibr">103</a>]. Copyright 2020 Elsevier and 2019 MDPI.</p>
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<p>Schematic representation of the SGNS@MPA synthesis and microplate-based SERS detection platform for creatinine detection in human saliva. Reprinted with permission from ref. [<a href="#B113-biosensors-14-00564" class="html-bibr">113</a>]. Copyright 2024 Elsevier.</p>
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<p>Schematic illustration of the preparation process for the AgNPs/MIL-101 (Fe) hybrid structure (<b>A</b>) and schematic diagram of the detection of DA based on SERS (<b>B</b>). Reprinted with permission from ref. [<a href="#B122-biosensors-14-00564" class="html-bibr">122</a>]. Copyright 2015 ACS.</p>
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13 pages, 3049 KiB  
Article
A Facile Microwave-Promoted Formation of Highly Photoresponsive Au-Decorated TiO2 Nanorods for the Enhanced Photo-Degradation of Methylene Blue
by Andreea Bondarev, Sonia Mihai, Abubakar Katsina Usman, Diana Luciana Cursaru, Dănuţa Matei, Veronica Sătulu, Cătălina Gheorghe, Gheorghe Brănoiu and Raluca Şomoghi
Nanomaterials 2024, 14(22), 1780; https://doi.org/10.3390/nano14221780 - 5 Nov 2024
Viewed by 866
Abstract
The integration of noble metal nanoparticles (NPs) effectively modifies the electronic properties of semiconductor photocatalysts, leading to improved charge separation and enhanced photocatalytic performance. TiO2 nanorods decorated with Au NPs were successfully synthesized using a cost-effective, rapid microwave-assisted method in H2 [...] Read more.
The integration of noble metal nanoparticles (NPs) effectively modifies the electronic properties of semiconductor photocatalysts, leading to improved charge separation and enhanced photocatalytic performance. TiO2 nanorods decorated with Au NPs were successfully synthesized using a cost-effective, rapid microwave-assisted method in H2O2 and HF media for methylene blue (MB) degradation under visible light illumination. X-ray diffraction (XRD), X-ray photoelectron spectroscopy (XPS), scanning electron microscopy (SEM), transmission electron microscopy (TEM), N2 physisorption, and UV–vis spectroscopy were employed to characterize the structures, morphologies, compositions, and photoelectronic properties of the as-synthesized materials. The fusing of Au NPs effectively alters the electronic structure of TiO2, enhancing the charge separation efficiency and improved electrical conductivity. The HF treatment promotes the exposure of the highly reactive (001) and (101) crystalline facets. The improved photocatalytic activity of Au/TiO2, achieving 97% efficiency, is attributed to the surface plasmon resonance (SPR) effect of the Au NPs and the presence of oxygen vacancies. The photodegradation of MB using the TiO2/Au photocatalysts follows pseudo-first-order kinetics, highlighting the enhanced catalytic efficiency of the synthesized nanostructures. The exceptional properties of the binary Au/TiO2 photocatalysts, including the SPR effect, exposed crystallographic faces, and efficient charge carrier separation through a decrease in the recombination of electrons and holes, contribute to the photocatalytic degradation of MB. Full article
(This article belongs to the Section Environmental Nanoscience and Nanotechnology)
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<p>Powder XRD patterns of Au/TiO<sub>2</sub> nanorods.</p>
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<p>XPS spectra: survey spectrum (<b>a</b>); deconvoluted Ti 2p spectra (<b>b</b>); deconvoluted O 1s spectra (<b>c</b>); deconvoluted Au 4f spectra (<b>d</b>).</p>
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<p>SEM images for yellow TiO<sub>2</sub> (nanorods) (<b>a</b>) and (<b>b</b>); Au/TiO<sub>2</sub> (<b>c</b>); EDS map for Au/TiO<sub>2</sub> (<b>d</b>).</p>
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<p>HR-TEM image: TiO<sub>2</sub> nanosheets (<b>a</b>,<b>b</b>); the corresponding FFT pattern (<b>c</b>); magnified lattice fringes for d-spacing calculation (101) (<b>d</b>); Au/TiO<sub>2</sub> (<b>e</b>); magnified lattice fringes for d-spacing calculation (111) Au (<b>f</b>).</p>
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<p>Nitrogen adsorption—desorption isotherms for yellow TiO<sub>2</sub> (black line) and Au/TiO<sub>2</sub> (red line). The detail represents the pore distribution for the TiO<sub>2</sub> (black line) and Au/TiO<sub>2</sub> (red line).</p>
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<p>Determination of band gap energy for Au/TiO<sub>2</sub> (<b>a</b>); yellow TiO<sub>2</sub> (<b>b</b>); UV-Vis absorption spectrum (<b>c</b>).</p>
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<p>Photodegradation efficiency of MB: without photocatalyst (blue line); yellow TiO<sub>2</sub> (red line); Au/TiO<sub>2</sub> (black line) (<b>a</b>); the pseudo-first-order kinetic rate plot (<b>b</b>).</p>
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<p>Photocatalytic stability (<b>a</b>); scavenger test (<b>b</b>).</p>
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11 pages, 1523 KiB  
Article
Diffusion-Induced Ordered Nanowire Growth: Mask Patterning Insights
by Kamila R. Bikmeeva and Alexey D. Bolshakov
Nanomaterials 2024, 14(21), 1743; https://doi.org/10.3390/nano14211743 - 30 Oct 2024
Viewed by 578
Abstract
Innovative methods for substrate patterning provide intriguing possibilities for the development of devices based on ordered arrays of semiconductor nanowires. Control over the nanostructures’ morphology in situ can be obtained via extensive theoretical studies of their formation. In this paper, we carry out [...] Read more.
Innovative methods for substrate patterning provide intriguing possibilities for the development of devices based on ordered arrays of semiconductor nanowires. Control over the nanostructures’ morphology in situ can be obtained via extensive theoretical studies of their formation. In this paper, we carry out an investigation of the ordered nanowires’ formation kinetics depending on the growth mask geometry. Diffusion equations for the growth species on both substrate and nanowire sidewalls depending on the spacing arrangement of the nanostructures and deposition rate are considered. The value of the pitch corresponding to the maximum diffusion flux from the substrate is obtained. The latter is assumed to be the optimum in terms of the nanowire elongation rate. Further study of the adatom kinetics demonstrates that the temporal dependence of a nanowire’s length is strongly affected by the ratio of the adatom’s diffusion length on the substrate and sidewalls, providing insights into the proper choice of a growth wafer. The developed model allows for customization of the growth protocols and estimation of the important diffusion parameters of the growth species. Full article
(This article belongs to the Section Theory and Simulation of Nanostructures)
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<p>Schematic representation of the NW VLS growth. <span class="html-italic">J</span> is the growth flux promoting direct impingement of the growth species into a catalyst. Droplet (<b>a</b>) <span class="html-italic">j<sub>diff(s)</sub></span> corresponds to the diffusion flux from substrate to a NW; <span class="html-italic">j<sub>diff(sw)</sub></span>—diffusion flux on the NW sidewalls; (<b>b</b>) 1/<span class="html-italic">τ<sub>s</sub></span> corresponds to the desorption rate with the adatom lifetime <span class="html-italic">τ<sub>s</sub></span> on the substrate; <span class="html-italic">R</span>—NW radius; (<b>c</b>) 1/<span class="html-italic">τ<sub>sw</sub></span> corresponds to the desorption rate with the adatom lifetime <span class="html-italic">τ<sub>sw</sub></span> on sidewalls; <span class="html-italic">P</span>—pitch (NW-to-NW disatance); <span class="html-italic">H</span>—NW length.</p>
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<p>Modeling results: substrate diffusion. (<b>a</b>) Distribution of adatoms’ concentration on a substrate for different substrate diffusion lengths: <span class="html-italic">R</span> = 100 nm; <span class="html-italic">P</span> = 1000 nm; <math display="inline"><semantics> <mrow> <mi mathvariant="sans-serif">Ω</mi> </mrow> </semantics></math> = 0.056 nm<sup>3</sup>; <span class="html-italic">V</span> = 1 ML/s; <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>D</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> = 250 nm<sup>2</sup>/s; <span class="html-italic">χ</span> = 1. Dependencies of the substrate diffusion flux on the distance between the NWs for different (<b>b</b>) substrate diffusion lengths calculated with the use of the parameters above and (<b>c</b>) impingement fluxes with the following parameters: <span class="html-italic">R</span> = 200 nm; <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>D</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> = 250 nm<sup>2</sup>/s; <math display="inline"><semantics> <mrow> <mi mathvariant="sans-serif">Ω</mi> <mo> </mo> </mrow> </semantics></math>= 0.056 nm<sup>3</sup>; <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> = 100 nm. (<b>d</b>) Normalized over <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> saturation pitch dependence on normalized NW radius: red dot are values calculated for <span class="html-italic">P</span>* corresponding to 0.9 <span class="html-italic">j<sub>max</sub></span>, blue are values for 0.95 <span class="html-italic">j<sub>max</sub></span>, and the red line corresponds to the equation <span class="html-italic">P</span>* = 3<math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> </mrow> </semantics></math> + 2<span class="html-italic">R</span>.</p>
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<p>Modeling results: NW growth. (<b>a</b>) Distribution of adatom concentration on the sidewalls for different sidewall diffusion lengths (considering <math display="inline"><semantics> <mrow> <mi>R</mi> <mo>=</mo> <mn>100</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>;</mo> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> </mrow> </msub> <mo>=</mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">s</mi> <mo>;</mo> <mi mathvariant="normal">Ω</mi> <mo>=</mo> <mn>0.05</mn> <mo> </mo> <msup> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msup> <mo>,</mo> <msub> <mrow> <mi>V</mi> <mo>=</mo> <mn>0.05</mn> <mo> </mo> <mstyle scriptlevel="0" displaystyle="true"> <mfrac> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mi mathvariant="normal">s</mi> </mrow> </mfrac> </mstyle> <mo>;</mo> <mo> </mo> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> </mrow> </msub> <mo>=</mo> <mn>100</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>;</mo> <msubsup> <mrow> <mi>n</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mo>′</mo> </mrow> </msubsup> <msub> <mrow> <mo stretchy="false">|</mo> </mrow> <mrow> <mi>r</mi> <mo>=</mo> <mi>R</mi> </mrow> </msub> <mo>=</mo> <mn>0.24</mn> <mo> </mo> <msup> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>3</mn> </mrow> </msup> <mo>;</mo> <mo> </mo> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">d</mi> <mo> </mo> <mi>P</mi> <mo>=</mo> <mn>1000</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>). (<b>b</b>) Dependence of the growth rate on NW length <span class="html-italic">H</span> with the following parameters: <math display="inline"><semantics> <mrow> <mi>R</mi> <mo>=</mo> <mn>50</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>;</mo> <msub> <mrow> <mi>D</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> </mrow> </msub> <mo>=</mo> <mstyle scriptlevel="0" displaystyle="true"> <mfrac> <mrow> <mn>200</mn> <mo> </mo> <msup> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msup> </mrow> <mrow> <mi mathvariant="normal">s</mi> </mrow> </mfrac> </mstyle> <mo>;</mo> <mi mathvariant="normal">Ω</mi> <mo>=</mo> <mn>0.05</mn> <mo> </mo> <msup> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mn>3</mn> </mrow> </msup> <mo>;</mo> <mi mathvariant="normal">V</mi> <mo>=</mo> <mn>0.05</mn> <mo> </mo> <mstyle scriptlevel="0" displaystyle="true"> <mfrac> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mi mathvariant="normal">s</mi> </mrow> </mfrac> </mstyle> <mo>,</mo> <msubsup> <mrow> <mi>n</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mo>′</mo> </mrow> </msubsup> <msub> <mrow> <mo stretchy="false">|</mo> </mrow> <mrow> <mi>r</mi> <mo>=</mo> <mi>R</mi> </mrow> </msub> <mo>=</mo> <mn>0.5</mn> <mo> </mo> <msup> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>3</mn> </mrow> </msup> <mo>;</mo> <mo> </mo> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">d</mi> <mo> </mo> <mi>P</mi> <mo>=</mo> <mn>1000</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>. (<b>c</b>) Time dependence of the normalized NW length (<span class="html-italic">H</span>/<math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> <mo> </mo> </mrow> </msub> </mrow> </semantics></math>) for the different sidewall diffusion lengths and corresponding <math display="inline"><semantics> <mrow> <mi>β</mi> </mrow> </semantics></math> values.</p>
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<p>Experimental data fitting. (<b>a</b>) InP NW elongation experimental data obtained in [<a href="#B35-nanomaterials-14-01743" class="html-bibr">35</a>]. Parameters of the experiment used in the modeling: deposition flux rate <span class="html-italic">V</span> = 0.04 nm/s, NW radius <span class="html-italic">R</span> = 12 nm, volume per atom pair <math display="inline"><semantics> <mrow> <mi mathvariant="sans-serif">Ω</mi> </mrow> </semantics></math> = 0.05 nm<sup>3</sup>. Fitting parameters: diffusion sidewall length <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> <mo> </mo> </mrow> </msub> </mrow> </semantics></math> = 1.0 μm, and diffusion coefficient <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>D</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> </mrow> </msub> </mrow> </semantics></math> = 20 nm<sup>2</sup>/s. (<b>b</b>) InGaAs NW elongation data obtained in [<a href="#B27-nanomaterials-14-01743" class="html-bibr">27</a>]; parameters of experiment: deposition flux rate <span class="html-italic">V</span> = 0.024 nm/s, radius <span class="html-italic">R</span> = 100 nm, pitch <span class="html-italic">P</span> = 1 μm, volume per atom pair <math display="inline"><semantics> <mrow> <mi mathvariant="sans-serif">Ω</mi> </mrow> </semantics></math> = 0.0556 nm<sup>3</sup>. Fitting parameters: diffusion sidewall length <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>λ</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> <mo> </mo> </mrow> </msub> </mrow> </semantics></math> = 250 nm, diffusion coefficient <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>D</mi> </mrow> <mrow> <mi>s</mi> <mi>w</mi> </mrow> </msub> </mrow> </semantics></math> = 200 nm<sup>2</sup>/s.</p>
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22 pages, 5361 KiB  
Article
Nanostructured Magnetite Coated with BiOI Semiconductor: Readiness Level in Advanced Solar Photocatalytic Applications for the Remediation of Phenolic Compounds in Wastewater from the Wine and Pisco Industry
by Alejandra Gallegos-Alcaíno, Gabriela Paz Barría, Yanko Moreno, Iván Fernández, Rodrigo Poblete, Héctor Maureira-Cortés, Antonia Cristal Figueroa Alvarado, Constanza Belén Hernández and José Flores
Appl. Sci. 2024, 14(21), 9898; https://doi.org/10.3390/app14219898 - 29 Oct 2024
Viewed by 949
Abstract
Heterogeneous photocatalysis is an advanced, efficient oxidation process that uses solar energy to be sustainable and low-cost compared to conventional wastewater treatments. This study synthesized BiOI/Fe3O4 using the solvothermal technique, evaluating stoichiometric ratios of Bi/Fe (2:1, 3:1, 5:1, and 7:1) [...] Read more.
Heterogeneous photocatalysis is an advanced, efficient oxidation process that uses solar energy to be sustainable and low-cost compared to conventional wastewater treatments. This study synthesized BiOI/Fe3O4 using the solvothermal technique, evaluating stoichiometric ratios of Bi/Fe (2:1, 3:1, 5:1, and 7:1) under simulated solar irradiation to optimize the degradation of caffeic acid, a pollutant found in wastewater from the wine and pisco industry. The nanomaterial with a 5:1 ratio (BF-5) was the most effective, achieving a degradation of 77.2% in 180 min. Characterization by X-ray Diffraction (XRD), Transmission Electron Microscopy (TEM), Brunauer–Emmett–Teller (BET), Barrett–Joyner–Halenda (BJH), Fourier Transform Infrared Spectroscopy (FTIR), Diffuse Reflectance Spectroscopy (DRS), and Vibrating Sample Magnetometry (VSM) showed that BF-5 has a porous three-dimensional structure with BiOI nanosheets coating the Fe3O4 surface, while retaining the pristine BiOI properties. The magnetite provided magnetic properties that facilitated the recovery of the photocatalyst, reaching 89.4% recovery. These findings highlight the potential of BF-5 as an efficient and recoverable photocatalyst for industrial applications. The technical, economic, and environmental feasibility were also evaluated at the technological readiness level (TRL) to project solar photocatalysis in real applications. Full article
(This article belongs to the Section Green Sustainable Science and Technology)
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Figure 1

Figure 1
<p>Experimental setup used during photocatalytic tests.</p>
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<p>Molecular structure of the model compound, caffeic acid.</p>
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<p>X-ray diffraction patterns of the synthesized materials: (<b>a</b>) Magnetite–Fe<sub>3</sub>O<sub>4</sub>, (<b>b</b>) individual BiOI, (<b>c</b>) BiOI/Fe<sub>3</sub>O<sub>4–</sub>BF-5.</p>
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<p>Images TEM (<b>a</b>) and (<b>b</b>) Fe<sub>3</sub>O<sub>4</sub>; (<b>c</b>) and (<b>d</b>) BiOI; (<b>e</b>) and (<b>f</b>) BF-5.</p>
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<p>N<sub>2</sub> adsorption–desorption isotherms (<b>a</b>) and pore size distribution (<b>b</b>) of BiOI pure, Fe<sub>3</sub>O<sub>4</sub>, and BF-5.</p>
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<p>Tauc Plot of the synthesized nanomaterials.</p>
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<p>FTIR spectra (<b>a</b>) BiOI; (<b>b</b>) Fe<sub>3</sub>O<sub>4</sub>; and (<b>c</b>) BF-5.</p>
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<p>VSM magnetization curve for Fe<sub>3</sub>O<sub>4</sub> and BF-5 (BiOI/Fe<sub>3</sub>O<sub>4</sub>).</p>
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<p>(<b>a</b>) Fe<sub>3</sub>O<sub>4</sub> and (<b>b</b>) BiOI/Fe<sub>3</sub>O<sub>4</sub> synthesized by the solvothermal method.</p>
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<p>Percentage of degradation after 180 min of the model pollutant under different Bi/Fe ratios.</p>
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<p>Comparison of the degradation of caffeic acid using pure BiOI, BiOI/Fe<sub>3</sub>O<sub>4</sub> 2:1; 3:1; 5:1; 7:1 (BF-2, BF-3, BF-5, BF-7, respectively), Fe<sub>3</sub>O<sub>4</sub>, and caffeic acid in the absence of a catalyst.</p>
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<p>Study sector located between 29° 20 and 32° 15 south latitude.</p>
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<p>(<b>a</b>) Photocatalytic system setup and (<b>b</b>) compound parabolic concentrator curve.</p>
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<p>Chile’s photovoltaic power potential (kWh/kWp). Notes: This figure shows Chile’s photovoltaic power potential, which refers to how much energy (kWh) is produced per kilowatt peak of a system. The figure was retrieved from <a href="https://globalsolaratlas.info" target="_blank">https://globalsolaratlas.info</a>. Solar resource data were obtained from the Global Solar Atlas. This map was published by the World Bank Group, funded by ESMAP, and prepared by Solargis (accessed 25 August 2024) [<a href="#B40-applsci-14-09898" class="html-bibr">40</a>].</p>
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<p>Technological Readiness Level (TRL) applied to the projections of this study focused on implementing heterogeneous photocatalysis using BiOI/Fe<sub>3</sub>O<sub>4</sub> in the wine and pisco industry.</p>
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