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11 pages, 7519 KiB  
Article
A Large-Scan-Range Electrothermal Micromirror Integrated with Thermal Convection-Based Position Sensors
by Anrun Ren, Yingtao Ding, Hengzhang Yang, Teng Pan, Ziyue Zhang and Huikai Xie
Micromachines 2024, 15(8), 1017; https://doi.org/10.3390/mi15081017 - 8 Aug 2024
Viewed by 263
Abstract
This paper presents the design, simulation, fabrication, and characterization of a novel large-scan-range electrothermal micromirror integrated with a pair of position sensors. Note that the micromirror and the sensors can be manufactured within a single MEMS process flow. Thanks to the precise control [...] Read more.
This paper presents the design, simulation, fabrication, and characterization of a novel large-scan-range electrothermal micromirror integrated with a pair of position sensors. Note that the micromirror and the sensors can be manufactured within a single MEMS process flow. Thanks to the precise control of the fabrication of the grid-based large-size Al/SiO2 bimorph actuators, the maximum piston displacement and optical scan angle of the micromirror reach 370 μm and 36° at only 6 Vdc, respectively. Furthermore, the working principle of the sensors is deeply investigated, where the motion of the micromirror is reflected by monitoring the temperature variation-induced resistance change of the thermistors on the substrate during the synchronous movement of the mirror plate and the heaters. The results show that the full-range motion of the micromirror can be recognized by the sensors with sensitivities of 0.3 mV/μm in the piston displacement sensing and 2.1 mV/° in the tip-tilt sensing, respectively. The demonstrated large-scan-range micromirror that can be monitored by position sensors has a promising prospect for the MEMS Fourier transform spectrometers (FTS) systems. Full article
(This article belongs to the Section A:Physics)
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Figure 1

Figure 1
<p>Schematic diagrams of different position sensing methods: (<b>a</b>) capacitive sensing [<a href="#B13-micromachines-15-01017" class="html-bibr">13</a>]; (<b>b</b>) piezoresistive sensing [<a href="#B19-micromachines-15-01017" class="html-bibr">19</a>]; (<b>c</b>) optical sensing [<a href="#B21-micromachines-15-01017" class="html-bibr">21</a>]; (<b>d</b>) inductive eddy current sensing [<a href="#B26-micromachines-15-01017" class="html-bibr">26</a>]; (<b>e</b>) piezoelectric sensing [<a href="#B29-micromachines-15-01017" class="html-bibr">29</a>].</p>
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<p>Schematic illustration of the electrothermal micromirror integrated with thermal convection-based position sensors.</p>
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<p>Working principles of the position sensors; (<b>a</b>–<b>c</b>) piston sensing; (<b>d</b>–<b>f</b>) tip-tilt sensing.</p>
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<p>Schematic diagrams of the Wheatstone bridge circuits: (<b>a</b>) piston sensing circuit. (<b>b</b>) tip-tilt sensing circuit.</p>
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<p>Schematic diagrams of the proposed device and the key components: (<b>a</b>) top view of the device; (<b>b</b>) enlarged view of the bimorph actuator; (<b>c</b>) 3D structure of the bimorph; (<b>d</b>) enlarged view of the position sensor and the critical structural parameters.</p>
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<p>Simulated temperature distributions of the position sensors during working at <span class="html-italic">T</span><sub>0</sub> = 293 K. (<b>a</b>,<b>b</b>) Piston sensing. (<b>c</b>,<b>d</b>) Tip-tilt sensing.</p>
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<p>Extracted temperature curves along the indicated lines in <a href="#micromachines-15-01017-f006" class="html-fig">Figure 6</a>: (<b>a</b>) piston sensing; (<b>b</b>) tip-tilt sensing.</p>
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<p>Temperature variations of the thermistors under different environment temperatures: (<b>a</b>) piston displacements; (<b>b</b>) optical scan angles.</p>
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<p>Fabrication process of the large-scan-range electrothermal micromirror integrated with position sensors. (<b>a</b>) PECVD oxide deposition and etching. (<b>b</b>) PECVD oxide deposition. (<b>c</b>) Pt sputtering and lift-off. (<b>d</b>) PECVD oxide deposition and etching. (<b>e</b>) Al sputtering and etching. (<b>f</b>) Oxide etching. (<b>g</b>) Backside Si etching. (<b>h</b>) Backside box layer etching. (<b>i</b>) Frontside Si isotropic etching.</p>
Full article ">Figure 10
<p>Images of the fabricated electrothermal micromirror integrated with position sensors: (<b>a</b>) the fabricated device after release; (<b>b</b>) the close-up view of the heater and the thermistor.</p>
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<p>Measured resistance-temperature curve for the Pt resistor in the bimorph.</p>
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<p>The quasi-static and dynamic responses of the micromirror: (<b>a</b>) piston displacement versus driving voltage; (<b>b</b>) optical angle versus driving voltage; (<b>c</b>) frequency response.</p>
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<p>Quasi-static measurement results: (<b>a</b>) the output of the position sensor and calibrated piston displacement versus the driving voltage of two actuators; (<b>b</b>) the output of the position sensor and calibrated optical scan range versus the driving voltage of one actuator.</p>
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16 pages, 1619 KiB  
Article
Fast Monitoring of Quality and Adulteration of Blended Sunflower/Olive Oils Applying Near-Infrared Spectroscopy
by Magdalena Klinar, Maja Benković, Tamara Jurina, Ana Jurinjak Tušek, Davor Valinger, Sandra Maričić Tarandek, Anamaria Prskalo, Juraj Tonković and Jasenka Gajdoš Kljusurić
Chemosensors 2024, 12(8), 150; https://doi.org/10.3390/chemosensors12080150 - 2 Aug 2024
Viewed by 355
Abstract
Food adulteration which is economically motivated (i.e., food fraud) is an incentive for the development and application of new and fast detection methods/instruments. An example of a fast method that is extremely environmentally friendly is near-infrared spectroscopy (NIRS). Therefore, the goal of this [...] Read more.
Food adulteration which is economically motivated (i.e., food fraud) is an incentive for the development and application of new and fast detection methods/instruments. An example of a fast method that is extremely environmentally friendly is near-infrared spectroscopy (NIRS). Therefore, the goal of this research was to examine the potential of its application in monitoring the adulteration of blended sunflower/olive oils and to compare two types of NIRS instruments, one of which is a portable micro-device, which could be used to assess the purity of olive oil anywhere and would be extremely useful to inspection services. Both NIR devices (benchtop and portable) enable absorbance monitoring in the wavelength range from 900 to 1700 nm. Extra virgin oils (EVOOs) and “ordinary” olive oils (OOs) from large and small producers were investigated, which were diluted with sunflower oil in proportions of 1–15%. However, with the appearance of different salad oils that have a defined share of EVOO stated on the label (usually 10%), the possibilities of the recognition and manipulation in these proportions were tested; therefore, EVOO was also added to sunflower oil in proportions of 1–15%. The composition of fatty acids, color parameters, and total dissolved substances and conductivity for pure and “adulterated” oils were monitored. Standard tools of multivariate analysis were applied, such as (i) analysis of main components for the qualitative classification of oil and (ii) partial regression using the least square method for quantitative prediction of the proportion of impurities and fatty acids. Qualitative models proved successful in classifying (100%) the investigated oils, regardless of whether the added thinner was olive or sunflower oil. Developed quantitative models relating measured parameters with the NIR scans, resulted in values of R2 ≥ 0.95 and was reliable (RPD > 8) for fatty acid composition prediction and for predicting the percentage of the added share of impurity oils, while color attributes were less successfully predicted with the portable NIR device (RPD in the range of 2–4.2). Although with the portable device, the prediction potentials remained at a qualitative level (e.g., color parameters), it is important to emphasize that both devices were tested not only with EVOO but also with OO and regardless of whether proportions of 1–15% sunflower oil were added to EVOO and OO or EVOO and OO in the same proportions to sunflower oil. Full article
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Figure 1
<p>3D presentation of the color space (L, a, and b) for sunflower and olive oils (in a pure form, as well as mixed (1–15%, 85–99% of added sunflower oil in olive oils)).</p>
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<p>Color changes in diluted olive oil samples (5–15% diluted samples were calculated according the standard olive oil and 85–95% according to sunflower oil).</p>
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<p>Grouping of samples based on the fatty acid composition and color parameters for adulterated oil samples.</p>
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<p>Measured vs. predicted shares of added olive oil in the sunflower oil, based on NIR scans of the benchtop NIR device and the portable one for blended sunflower oils with 1–15% olive oil (<b>A</b>) and 85–99% (<b>B</b>).</p>
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11 pages, 1648 KiB  
Article
Synthesis of New Complex Ferrite Li0.5MnFe1.5O4: Chemical–Physical and Electrophysical Research
by Mukhametkali Mataev, Altynai Madiyarova, Gennady Patrin, Moldir Abdraimova, Marzhan Nurbekova and Zhadyra Durmenbayeva
Materials 2024, 17(15), 3754; https://doi.org/10.3390/ma17153754 - 30 Jul 2024
Viewed by 409
Abstract
In this article, the sol–gel method was used as a synthesis method, which shows the physicochemical nature of the synthesis of a new complex material, ferrite Li0.5MnFe1.5O4. The structure and composition of the synthesized ferrite were determined [...] Read more.
In this article, the sol–gel method was used as a synthesis method, which shows the physicochemical nature of the synthesis of a new complex material, ferrite Li0.5MnFe1.5O4. The structure and composition of the synthesized ferrite were determined by X-ray phase analysis. According to analysis indicators, it was found that our compound is a single-phase, spinel-structured, and syngony-cubic type of compound. The microstructure of the compound and the quantitative composition of the elements contained within it were analyzed under a scanning electron microscope (SEM). Under a scanning electron microscope, microsystems were taken from different parts of Li0.5MnFe1.5O4-type crystallite; the elemental composition of crystals was analyzed; and the general type of surface layer of complex ferrite was shown. As a result, given the fact that the compound consists of a single phase, the clarity of its construction was determined by the topography and chemical composition of the compound. As a result, it was found that the newly synthesized complex ferrites correspond to the formula Li0.5MnFe1.5O4. The particles of the formed compounds have a large size (between 50.0 μm or 20.0 μm and 10.0 μm). Electrophysical measurements were carried out on an LCR-800 unit at intervals of 293–483 K and at frequencies of 1.5 and 10 kHz. An increase in frequency to 10 kHz led to a decrease in the value ε in the range of the studied temperature (293–483 K). Full article
(This article belongs to the Section Materials Chemistry)
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<p>X-ray diffractogram of the complex ferrite Li<sub>0.5</sub>MnFe<sub>1.5</sub>O<sub>4</sub>. Insert: phase ratio diagram.</p>
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<p>Image of the new mixed complex ferrite Li<sub>0.5</sub>MnFe<sub>1.5</sub>O<sub>4</sub> measured with three different micrometer accuracies: (<b>a</b>) 10 μm; (<b>b</b>) 20 μm; (<b>c</b>) 50 μm.</p>
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<p>Spectrum samples of the Li<sub>0.5</sub>MnFe<sub>1.5</sub>O<sub>4</sub> compound. The results of the element analysis are built-in.</p>
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<p>Dependence of dielectric constant (<b>a</b>) and electrical resistance (<b>b</b>) on temperature and frequency equal to 1 kHz.</p>
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35 pages, 15757 KiB  
Article
Near-Complete Sampling of Forest Structure from High-Density Drone Lidar Demonstrated by Ray Tracing
by Dafeng Zhang, Kamil Král, Martin Krůček, K. C. Cushman and James R. Kellner
Remote Sens. 2024, 16(15), 2774; https://doi.org/10.3390/rs16152774 - 29 Jul 2024
Viewed by 418
Abstract
Drone lidar has the potential to provide detailed measurements of vertical forest structure throughout large areas, but a systematic evaluation of unsampled forest structure in comparison to independent reference data has not been performed. Here, we used ray tracing on a high-resolution voxel [...] Read more.
Drone lidar has the potential to provide detailed measurements of vertical forest structure throughout large areas, but a systematic evaluation of unsampled forest structure in comparison to independent reference data has not been performed. Here, we used ray tracing on a high-resolution voxel grid to quantify sampling variation in a temperate mountain forest in the southwest Czech Republic. We decoupled the impact of pulse density and scan-angle range on the likelihood of generating a return using spatially and temporally coincident TLS data. We show three ways that a return can fail to be generated in the presence of vegetation: first, voxels could be searched without producing a return, even when vegetation is present; second, voxels could be shadowed (occluded) by other material in the beam path, preventing a pulse from searching a given voxel; and third, some voxels were unsearched because no pulse was fired in that direction. We found that all three types existed, and that the proportion of each of them varied with pulse density and scan-angle range throughout the canopy height profile. Across the entire data set, 98.1% of voxels known to contain vegetation from a combination of coincident drone lidar and TLS data were searched by high-density drone lidar, and 81.8% of voxels that were occupied by vegetation generated at least one return. By decoupling the impacts of pulse density and scan angle range, we found that sampling completeness was more sensitive to pulse density than to scan-angle range. There are important differences in the causes of sampling variation that change with pulse density, scan-angle range, and canopy height. Our findings demonstrate the value of ray tracing to quantifying sampling completeness in drone lidar. Full article
(This article belongs to the Section Forest Remote Sensing)
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Figure 1
<p>(<b>A</b>) Flight lines from drone lidar in a temperate mountain forest in the southwest Czech Republic. We completed two sets of orthogonal flight lines. (<b>B</b>) Locations of TLS scans and 100 m<sup>2</sup> plots used in this study. (<b>C</b>) The 100 m<sup>2</sup> plots used in this study in relation to censused stems. The point size of the censused stems is proportional to DBH (unit: cm).</p>
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<p>High-resolution forest structure from a high-density drone. Squares are 0.5 m voxels. Voxels were classified into four categories using non-ground returns from drone lidar: voxels with one or more returns (green), voxels that were searched by laser pulses and contained no return (yellow), voxels with only occluded pulses (blue), and voxels with no returns, laser pulses, or occluded pulses (white). Grey dots on green voxels represent lidar returns. Darker grey dots indicate more returns in the voxel.</p>
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<p>Voxel traversal and voxel type determination. (<b>A</b>) Illustration of voxel traversal in a 2-D view featuring nine voxels and a laser pulse generating a return. All the squares represent occupied voxels. The solid yellow line segment represents a pulse trajectory. The green dot represents a lidar return. The black dot is the starting point of the pulse trajectory. Letters a–i are labels for the voxels. (<b>B</b>) Relationships among the voxels depicted in (<b>A</b>).</p>
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<p>Sampling completeness (the proportion of occupied voxels that were detected) as a function of pulse density and scan-angle range (plot 1). (<b>A</b>) When scan-angle range was decoupled from pulse density, sampling completeness was more strongly associated with pulse density than with scan-angle range. (<b>B</b>) Sampling completeness when scan-angle range was not decoupled from pulse density. Missing data points in (<b>A</b>) are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
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<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range (plot 1). On each of the six panels, from left to right, the black dots represent pulse densities of 1, 10, 50, 100, 200, 300, 400, 500, 1000, 1500 pulses/m<sup>2</sup>. Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure 6
<p>Proportions of different types of undetected voxels under different pulse densities and scan-angle ranges (plot 1). (<b>A</b>) Undetected and unsearched voxels. (<b>B</b>) Undetected and searched voxels. (<b>C</b>) Undetected and unobserved voxels. (<b>D</b>) Undetected and completely occluded voxels. Missing data points in each panel are associated with small sample sizes at some combinations of scan-angle range and pulse density. The number of undetected and unsearched voxels (<b>A</b>) is equal to the number of undetected and unobserved voxels (<b>C</b>) plus the number of undetected and completely occluded voxels (<b>D</b>).</p>
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<p>Proportions of occupied voxels that were detected or undetected as a function of pulse density and scan-angle range at multiple heights above ground (Plot 1). Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density. The number of occupied voxels at each height (i.e., the denominator for calculating proportions of different undetected voxels at each height) is shown in <a href="#remotesensing-16-02774-f0A15" class="html-fig">Figure A15</a>.</p>
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<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at multiple heights above ground (plot 1). Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density. The number of occupied voxels at each height (i.e., the denominator for calculating proportions of different undetected voxels at each height) is shown in <a href="#remotesensing-16-02774-f0A15" class="html-fig">Figure A15</a>.</p>
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<p>The proportion of undetected and searched voxels at different heights as a function of pulse density and scan-angle range in the 100 m<sup>2</sup> plot (Plot 1). Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure 10
<p>The proportion of undetected and completely occluded voxels at different heights as a function of pulse density and scan-angle range in the 100 m<sup>2</sup> plot (Plot 1). Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at some combinations of scan-angle range and pulse density.</p>
Full article ">Figure A1
<p>Stem and branch structure as a function of pulse density and scan-angle range. The area is approximately 30 by 30 m in a temperate mountain forest in the southwest Czech Republic. The number of returns was more sensitive to pulse density than to scan-angle range.</p>
Full article ">Figure A2
<p>Stem and branch structure as a function of pulse density and scan-angle range, highlighting vegetation structure among prominent stems. Data are from high-density drone lidar in a temperate mountain forest in the southwest Czech Republic. The number of returns was more sensitive to pulse density than to scan-angle range.</p>
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<p>Stem and branch structure as a function of pulse density and scan-angle range, highlighting upper-canopy vegetation. Data are from high-density drone lidar in a temperate mountain forest in the southwest Czech Republic. The number of returns was more sensitive to pulse density than to scan-angle range.</p>
Full article ">Figure A4
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at Plot 2. On each of the six panels, from left to right, the black dots represent pulse densities of 1, 10, 50, 100, 200, 300, 400, 500, 1000, 1500 pulses/m<sup>2</sup>. Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50°, and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A5
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at Plot 3. On each of the six panels, from left to right, the black dots represent pulse densities of 1, 10, 50, 100, 200, 300, 400, 500, 1000, 1500 pulses/m<sup>2</sup>. Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50°, and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A6
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at Plot 4. On each of the six panels, from left to right, the black dots represent pulse densities of 1, 10, 50, 100, 200, 300, 400, 500, 1000, 1500 pulses/m<sup>2</sup>. Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50°, and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling its impact from pulse density. Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A7
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and azimuth-angle range (Plot 1). The azimuth-angle ranges were 0°–90°, 90°–180°, 180°–270°, and 270°–360°; they are labeled on the X-axis by the right bound (i.e., 90, 180, 270, 360, respectively). Missing data points are associated with small sample sizes at certain combinations of azimuth-angle range and pulse density.</p>
Full article ">Figure A8
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and azimuth-angle range (Plot 2). The azimuth-angle ranges were 0°–90°, 90°–180°, 180°–270°, and 270°–360°; they are labeled on the X-axis by the right bound (i.e., 90, 180, 270, 360, respectively). Missing data points are associated with small sample sizes at certain combinations of azimuth-angle range and pulse density.</p>
Full article ">Figure A9
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and azimuth-angle range (Plot 3). The azimuth-angle ranges were 0°–90°, 90°–180°, 180°–270°, and 270°–360°; they are labeled on the X-axis by the right bound (i.e., 90, 180, 270, 360, respectively). Missing data points are associated with small sample sizes at certain combinations of azimuth-angle range and pulse density.</p>
Full article ">Figure A10
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and azimuth-angle range (Plot 4). The azimuth-angle ranges were 0°–90°, 90°–180°, 180°–270°, and 270°–360°; they are labeled on the X-axis by the right bound (i.e., 90, 180, 270, 360, respectively). Missing data points are associated with small sample sizes at certain combinations of azimuth-angle range and pulse density.</p>
Full article ">Figure A11
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at multiple heights above ground in a 100 m<sup>2</sup> plot (Plot 2). Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A12
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at multiple heights above ground in a 100 m<sup>2</sup> plot (Plot 3). Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A13
<p>Proportions of occupied voxels that were detected and undetected as a function of pulse density and scan-angle range at multiple heights aboveground in a 100 m<sup>2</sup> plot (Plot 4). Missing data points are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
Full article ">Figure A14
<p>The proportion of detected voxels at different heights as a function of pulse density and scan-angle range in the 1 ha plot. Only 6 levels of scan-angle range (±10°, ±20°, ±30°, ±40°, ±50° and ±60°) are shown here because <a href="#remotesensing-16-02774-f004" class="html-fig">Figure 4</a> shows the limited impact of scan-angle range after decoupling from pulse density. Missing data points are associated with small sample sizes at some combinations of scan-angle range and pulse density.</p>
Full article ">Figure A15
<p>The number of occupied voxels at each height above ground in a 100 m<sup>2</sup> plot (Plot 1).</p>
Full article ">Figure A16
<p>Proportions of occluded pulses in undetected and searched voxels as a function of pulse density and scan-angle range (Plot 1). Missing panels are associated with small sample sizes at certain combinations of scan-angle range and pulse density.</p>
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14 pages, 13365 KiB  
Article
Detection of Copper Ions in Seawater Using a Graphitised Multi-Walled Carbon Nanotubes-Copper Ion Carrier Modified Electrode
by Chao Zhang, Wei Tao, Chengjun Qiu, Wei Qu, Yuan Zhuang, Yang Gu, Huili Hao and Zizi Zhao
Water 2024, 16(15), 2128; https://doi.org/10.3390/w16152128 - 27 Jul 2024
Viewed by 381
Abstract
Copper is an essential element in living organisms and is crucial in marine ecosystems. However, excessive concentrations can lead to seawater pollution and pose a risk of toxicity to marine organisms, as it is a heavy metal. In addition, it can enter the [...] Read more.
Copper is an essential element in living organisms and is crucial in marine ecosystems. However, excessive concentrations can lead to seawater pollution and pose a risk of toxicity to marine organisms, as it is a heavy metal. In addition, it can enter the human body through the food chain, potentially endangering human health. Consequently, there is increasing focus on the rapid and highly sensitive detection of copper ions (Cu2+). We prepared a graphite carbon electrode modified with graphitised multi-walled carbon nanotubes/copper(II) ion carrier IV (GMWCNT/copper(II) ion carrier IV/glassy carbon electrode (GCE)) using a drop-coating method. Scanning electron microscopy (SEM) analysis revealed that the composite material film possessed a large surface area. Incorporating this composite material significantly enhanced the adsorption capacity for ions on the electrode surface and greatly improved conductivity. Differential pulse anodic stripping voltammetry (DPASV) was employed to quantify copper levels in seawater. Under optimal experimental conditions, a strong linear relationship was observed between the Cu2+ response peak current and its concentration within a range of 50–500 µg L−1, with a correlation coefficient of 0.996. The GMWCNT/copper(II) ion carrier IV/GCE exhibited excellent stability and reproducibility, achieving a low detection limit for Cu2+ at 0.74 µg L−1 when applied to copper detection in seawater. Furthermore, spiked recovery rates ranging from 98.6% to 102.8% demonstrated the method’s high sensitivity, convenient operation, and practical value for real-world applications in detecting Cu2+ levels in seawater. Full article
(This article belongs to the Section Oceans and Coastal Zones)
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Figure 1
<p>Schematic diagram of detection mechanism.</p>
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<p>SEM images of the GMWCNT materials.</p>
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<p>SEM images of the GMWCNT/copper(II) ion carrier IV composite material.</p>
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<p>The cyclic voltammetric curve of various electrodes in 0.1 mol L<sup>−1</sup> potassium ferricyanide solution.</p>
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<p>CV curves of the GMWCNT/copper(II) ion carrier IV/GCE in 0.1 mol L<sup>−1</sup> potassium ferricyanide solution at various cycles.</p>
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<p>(<b>a</b>) CV responses of GMWCNT/copper(II) ion carrier IV/GCE at various scan rates in 0.1 mol L<sup>−1</sup> potassium ferricyanide solution. (<b>b</b>) Standard curve relating peak current to scan rate.</p>
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<p>DPSV plot of different electrodes in a sodium acetate solution containing 500 μg L<sup>−1</sup> of Cu<sup>2+</sup>.</p>
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<p>(<b>a</b>) Effect of deposition potential on the Cu<sup>2+</sup> response peak current. (<b>b</b>) Effect of deposition time on the Cu <sup>2+</sup> response peak current.</p>
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<p>Effects of different pH values.</p>
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<p>Effect of the membrane thickness.</p>
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<p>(<b>a</b>) Plot of GMWCNT/copper(II) ion carrier IV/GCE Cu<sup>2+</sup> at different concentrations (50 to 500 μg L<sup>−1</sup>); (<b>b</b>) corresponding linear regression curves.</p>
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<p>Stability test results of the same modified electrode in 100 µg L<sup>−1</sup> Cu<sup>2+</sup> over eight consecutive measurements.</p>
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<p>Stability of GMWCNT/copper(II) ion carrier IV/GCE by 30-day continuous assay.</p>
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<p>Reproducibility of different modified electrodes in 150 μg L<sup>−1</sup> Cu<sup>2+</sup>.</p>
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<p>Charge transfer processes of the GMWCNT/copper(II) ion carrier IV/GCE, GCE, GR/GCE, and GMWCNT/GCE in a 0.1 Mol KCl solution of 1 mMol K<sub>3</sub>[Fe(CN)<sub>6</sub>].</p>
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<p>Peak current of Cu(II) solution after the addition of a 100-fold concentration of Zn(II), Cr(II), Pb(II), and Cd(II) interfering ions.</p>
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11 pages, 14388 KiB  
Article
Investigation of Defect Formation in Monolithic Integrated GaP Islands on Si Nanotip Wafers
by Ines Häusler, Rostislav Řepa, Adnan Hammud, Oliver Skibitzki and Fariba Hatami
Electronics 2024, 13(15), 2945; https://doi.org/10.3390/electronics13152945 - 26 Jul 2024
Viewed by 372
Abstract
The monolithic integration of gallium phosphide (GaP), with its green band gap, high refractive index, large optical non-linearity, and broad transmission range on silicon (Si) substrates, is crucial for Si-based optoelectronics and integrated photonics. However, material mismatches, including thermal expansion mismatch and polar/non-polar [...] Read more.
The monolithic integration of gallium phosphide (GaP), with its green band gap, high refractive index, large optical non-linearity, and broad transmission range on silicon (Si) substrates, is crucial for Si-based optoelectronics and integrated photonics. However, material mismatches, including thermal expansion mismatch and polar/non-polar interfaces, cause defects such as stacking faults, microtwins, and anti-phase domains in GaP, adversely affecting its electronic properties. Our paper presents a structural and defect analysis using scanning transmission electron microscopy, high-resolution transmission electron microscopy, and scanning nanobeam electron diffraction of epitaxial GaP islands grown on Si nanotips embedded in SiO2. The Si nanotips were fabricated on 200 mm n-type Si (001) wafers using a CMOS-compatible pilot line, and GaP islands were grown selectively on the tips via gas-source molecular-beam epitaxy. Two sets of samples were investigated: GaP islands nucleated on open Si nanotips and islands nucleated within self-organized nanocavities on top of the nanotips. Our results reveal that in both cases, the GaP islands align with the Si lattice without dislocations due to lattice mismatch. Defects in GaP islands are limited to microtwins and stacking faults. When GaP nucleates in the nanocavities, most defects are trapped, resulting in defect-free GaP islands. Our findings demonstrate an effective approach to mitigate defects in epitaxial GaP on Si nanotip wafers fabricated by CMOS-compatible processes. Full article
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<p>The tilted-view SEM images depict two GaP/Si samples grown under similar conditions. (<b>a</b>) GaP islands grown on open Si tips and (<b>b</b>) GaP islands on self-organized cavities atop the Si tips. In these SEM images, dark gray areas correspond to the SiO<sub>2</sub> mask, while the bright gray islands represent GaP. The insets show the cross-sectional schematic layout of a single island for both scenarios: islands grown on open Si tips (<b>a</b>) and islands protruding from the cavities (<b>b</b>).</p>
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<p>Cross-sectional TEM images of the Si tips and the GaP islands. (<b>a.1</b>) Open Si tips prior to GaP growth; (<b>a.2</b>–<b>a.7</b>) GaP islands grown on open Si tips; (<b>b.1</b>) Si tip with a cavity on top of that prior to GaP growth; and (<b>b.2</b>–<b>b.7</b>) GaP islands grown on the cavities.</p>
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<p>Exemplary element analysis using energy dispersive X-ray spectroscopy of island #2 and island #8 (<a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>(a.3,b.3)). (<b>a.1</b>,<b>b.1</b>) are the Bright-Field STEM images from island #2 and island #8. The distribution maps for Silicon (<b>a.2</b>,<b>b.2</b>), Oxygen (<b>a.3</b>,<b>b.3</b>), Gallium (<b>a.4</b>,<b>b.4</b>), Phosphorus (<b>a.5</b>,<b>b.5</b>), and Platinum (<b>a.6</b>,<b>b.6</b>) are displayed using yellow, green, red, blue, and violet colors, respectively. The corresponding edges used for generating these maps are indicated next to each element’s name above the maps.</p>
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<p>Exemplary element analysis using energy dispersive X-ray spectroscopy of island #5 and island #7 (<a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>(a.6,b.2)). (<b>a.1</b>,<b>b.1</b>) are the Bright-Field STEM images from island #5 and island #7. The distribution maps for Silicon (<b>a.2</b>,<b>b.2</b>), Oxygen (<b>a.3</b>,<b>b.3</b>), Gallium (<b>a.4</b>,<b>b.4</b>), Phosphorus (<b>a.5</b>,<b>b.5</b>), and Platinum (<b>a.6</b>,<b>b.6</b>) are displayed using yellow, green, red, blue, and violet colors, respectively. The corresponding edges used for generating these maps are indicated next to each element’s name above the maps.</p>
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<p>Analysis of phase and orientation using scanning nanobeam diffraction (SNBD) of island #2 and island #8 (<a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>(a.3,b.3)). (<b>a.1</b>,<b>b.1</b>): Virtual Bright-Field STEM images from island #2 and island #8, respectively. (<b>a.2</b>,<b>b.2</b>): Corresponding phase maps of the islands. (<b>a.3</b>–<b>a.5</b>,<b>b.3</b>–<b>b.5</b>) show the orientation maps in three different directions. The color code on the right side represents the crystallographic direction of the cubic structures.</p>
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<p>Analysis of phase and orientation using scanning nanobeam diffraction (SNBD) of island #5 (<a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>(a.6)) and island #7 (<a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>(b.2)). (<b>a.1</b>,<b>b.1</b>): Virtual Bright-Field STEM images from island #5 and island #7, respectively. (<b>a.2</b>,<b>b.2</b>): Corresponding phase maps of the islands. (<b>a.3</b>–<b>a.5</b>,<b>b.3</b>–<b>b.5</b>) show the orientation maps in three different directions. The color code on the right side represents the crystallographic direction of the cubic structures.</p>
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<p>Structural analysis of an exemplary defect-rich island (island#5 in <a href="#electronics-13-02945-f002" class="html-fig">Figure 2</a>). (<b>a</b>) Overview cross-sectional TEM image of the island. (<b>b</b>) High-resolution TEM of GaP structure around the Si tip. (<b>c</b>) Analysis of the HRTEM image of the area marked in the yellow square in part (<b>b</b>). The HRTEM image is divided into five segments, each separated by defect lines. From each segment, a representative area, delineated by colored squares, was selected for FFT analysis (see insets). Surrounding the HRTEM image are depictions of structures with their respective unit cells. A consistent cubic GaP structure with [110] orientation was observed across all areas. The crystallographic indexing of the interfaces between areas is shown. The unit cells for each crystallographic plane are drawn in the same color as the one used to underline the respective plane. The transitions of individual segments are dominated by stacking faults on the {111} planes.</p>
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15 pages, 6538 KiB  
Article
rGO/MWCNT-COOH-Modified Electrodes for the Detection of Trace Cd(II) and Zn(II) in Coastal Seawater
by Yang Gu, Chengjun Qiu, Wei Qu, Wei Tao, Zizi Zhao and Huili Hao
Water 2024, 16(14), 2026; https://doi.org/10.3390/w16142026 - 17 Jul 2024
Viewed by 477
Abstract
Cadmium (Cd) and zinc (Zn) in seawater enter the human body through the food chain. Combined toxicity tests indicated that high concentrations of Cd(II) and low concentrations of Zn(II) had a synergistic effect on humans. Thus, there is an urgent need to prepare [...] Read more.
Cadmium (Cd) and zinc (Zn) in seawater enter the human body through the food chain. Combined toxicity tests indicated that high concentrations of Cd(II) and low concentrations of Zn(II) had a synergistic effect on humans. Thus, there is an urgent need to prepare a sensor for rapid and simultaneous detection of Cd(II) and Zn(II) in seawater. Herein, a reduced graphene oxide/carboxylated multi-walled carbon nanotube (rGO/MWCNT-COOH)-modified glassy carbon electrode was prepared in the experiments using the dropping method. The synthesis of various materials achieved the purpose of expanding the surface area, and scanning electron microscopy was used to observe the structure of the composite membrane. Moreover, the large number of functional groups on the surface of the composite membrane can also increase the adsorption of ions. For the determination of trace cadmium (II) and zinc (II) in seawater, the method used was differential pulse voltammetry (DPV). The results show that the peak current, which was obtained in the range of 5–400 μg/L for Cd(II) and Zn(II), has a linear relationship with concentration, corresponding to the detection limits of 0.8 μg/L for Cd(II) and 0.98 μg/L for Zn(II). The modified electrode was used to determine the Cd(II) and Zn(II) content in the coastal seawater of the Maowei Sea, and the recovery rate was between 95.8 and 98.2% for Cd(II) and 96.7~99.4% for Zn(II), which provided a novel approach of detection to define trace Cd(II) and Zn(II) in seawater. Full article
(This article belongs to the Special Issue Wastewater Treatment: Advanced Methods, Techniques and Processes)
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<p>Schematic diagram of detection mechanism.</p>
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<p>(<b>a</b>) Cyclic voltammetric curve of GO/GCE in a 0.1 mol/L potassium ferricyanide solution. (<b>b</b>) Cyclic voltammetric curve of MWCNT-COOH/GCE in a 0.1 mol/L potassium ferricyanide solution. (<b>c</b>) Cyclic voltammetric curve of rGO/MWCNT-COOH/GCE in a 0.1 mol/L potassium ferricyanide solution.</p>
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<p>(<b>a</b>) Cyclic voltammetric curve of GO/GCE in a 0.1 mol/L potassium ferricyanide solution. (<b>b</b>) Cyclic voltammetric curve of MWCNT-COOH/GCE in a 0.1 mol/L potassium ferricyanide solution. (<b>c</b>) Cyclic voltammetric curve of rGO/MWCNT-COOH/GCE in a 0.1 mol/L potassium ferricyanide solution.</p>
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<p>(<b>a</b>) rGO/MWCNT-COOH/GCE SEM material. (<b>b</b>) MWCNT-COOH/GCE SEM material.</p>
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<p>DPSV plot of the different electrodes in a solution of sodium acetate containing 500 μg/L of Cd(II) and Zn(II).</p>
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<p>(<b>a</b>) Effect of different pH values on Cd(II). (<b>b</b>) Effect of different pH values on Zn(II).</p>
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<p>(<b>a</b>) Effect of accumulation potential on Cd(II). (<b>b</b>) Effect of accumulation potential on Zn(II).</p>
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<p>(<b>a</b>) Effect of accumulation time on Cd(II). (<b>b</b>) Effect of accumulation time on Zn(II).</p>
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<p>(<b>a</b>) Effect of membrane thickness on Cd(II). (<b>b</b>) Effect of membrane thickness on Zn(II).</p>
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<p>Voltammogram of rGO/MWCNT-COOH/GCE on the dissolution of Cd(II) and Zn(II) at different concentrations (5–400 μg/L).</p>
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<p>(<b>a</b>) Linear regression curves for Cd(II). (<b>b</b>) Linear regression curves for Zn(II).</p>
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<p>(<b>a</b>) Eight stability changes of the same modified electrode in 100 μg/L of Cd(II). (<b>b</b>) Eight stability changes of the same modified electrode in 100 μg/L of Zn(II).</p>
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<p>(<b>a</b>) Reproducibility of different modified electrodes in 150 μg/L of Cd(II). (<b>b</b>) Reproducibility of different modified electrodes in 150 μg/L of Zn(II).</p>
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15 pages, 5750 KiB  
Article
The First Observation of the Filamentous Fungus Neurospora crassa Growing in the Roots of the Grass Brachypodium distachyon
by Krisztina Kollath-Leiß, Urska Repnik, Hannes Winter, Heinrich Winkelmann, Anna Sophia Freund and Frank Kempken
J. Fungi 2024, 10(7), 487; https://doi.org/10.3390/jof10070487 - 14 Jul 2024
Viewed by 854
Abstract
The model organism Neurospora crassa has been cultivated in laboratories since the 1920s and its saprotrophic lifestyle has been established for decades. However, beyond their role as saprotrophs, fungi engage in intricate relationships with plants, showcasing diverse connections ranging from mutualistic to pathogenic. [...] Read more.
The model organism Neurospora crassa has been cultivated in laboratories since the 1920s and its saprotrophic lifestyle has been established for decades. However, beyond their role as saprotrophs, fungi engage in intricate relationships with plants, showcasing diverse connections ranging from mutualistic to pathogenic. Although N. crassa has been extensively investigated under laboratory conditions, its ecological characteristics remain largely unknown. In contrast, Brachypodium distachyon, a sweet grass closely related to significant crops, demonstrates remarkable ecological flexibility and participates in a variety of fungal interactions, encompassing both mutualistic and harmful associations. Through a comprehensive microscopic analysis using electron, fluorescence, and confocal laser scanning microscopy, we discovered a novel endophytic interaction between N. crassa and B. distachyon roots, where fungal hyphae not only thrive in the apoplastic space and vascular bundle but also may colonize plant root cells. This new and so far hidden trait of one of the most important fungal model organisms greatly enhances our view of N. crassa, opening new perspectives concerning the fungus‘ ecological role. In addition, we present a new tool for studying plant–fungus interspecies communication, combining two well-established model systems, which improves our possibilities of experimental design on the molecular level. Full article
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<p>Growth of <span class="html-italic">B. distachyon</span> roots with (blue) and without (orange) <span class="html-italic">N. crassa</span> co-cultivation. The red dashed line represents the time point, at which <span class="html-italic">N. crassa</span> spatially reaches the roots in the co-cultivation experiment. Significant differences between roots in the same developmental stage (grouped by boxes) are depicted as *** (<span class="html-italic">p</span> &lt; 0.005).</p>
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<p>The SEM visualization of <span class="html-italic">B. distachyon</span> roots infected with <span class="html-italic">N. crassa</span>. Roots are wrapped in a dense network of hyphae (<b>A</b>–<b>D</b>) and scattered with oval-shaped conidia (<b>C</b>–<b>H</b>). Hyphae of different thickness can be observed (<b>E</b>). The integrity of the root surface is preserved (<b>F</b>). Protoperithecia (encircled) form in the vicinity of a root (<b>B</b>,<b>D</b>,<b>G</b>). The Microconidia production of old hyphae (<b>H</b>). Asterisk (<b>*</b>): hypha; circle: protoperithecium; white arrow: root hair.</p>
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<p>Fluorescent images of longitudinal <span class="html-italic">B. distachyon</span> root sections co-cultivated with the <span class="html-italic">N. crassa</span> FGSC #9518 strain, expressing GFP-coupled histone1 protein. Additional green fluorescence results from the auto-fluorescing plant cell wall. (<b>A</b>) Confocal laser scanning images show apoplastic (red arrows) and subcellular (yellow arrows) growth of fungal hyphae. (<b>B</b>) Fluorescent microscopic images show <span class="html-italic">N. crassa</span> accumulation in single cortical plant cells. (<b><span class="html-italic">i–iii</span></b>) GFP channel, (<b><span class="html-italic">I–III</span></b>) corresponding brightfield images. (<b>C</b>,<b>D</b>) Spinning-disk confocal microscopy was used to present an overview of a larger root section area. Distinct sectors (depicted by red boxes) with invasive <span class="html-italic">N. crassa</span> growth (yellow arrows) are magnified. Blue arrows indicate the extensive hyphal network covering the root surface.</p>
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<p>Fluorescent images of longitudinal <span class="html-italic">B. distachyon</span> root sections co-cultivated with the <span class="html-italic">N. crassa</span> FGSC #9518 strain, expressing GFP-coupled histone1 protein. Additional green fluorescence results from the auto-fluorescing plant cell wall. (<b>A</b>) Confocal laser scanning images show apoplastic (red arrows) and subcellular (yellow arrows) growth of fungal hyphae. (<b>B</b>) Fluorescent microscopic images show <span class="html-italic">N. crassa</span> accumulation in single cortical plant cells. (<b><span class="html-italic">i–iii</span></b>) GFP channel, (<b><span class="html-italic">I–III</span></b>) corresponding brightfield images. (<b>C</b>,<b>D</b>) Spinning-disk confocal microscopy was used to present an overview of a larger root section area. Distinct sectors (depicted by red boxes) with invasive <span class="html-italic">N. crassa</span> growth (yellow arrows) are magnified. Blue arrows indicate the extensive hyphal network covering the root surface.</p>
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<p>The histological analysis of <span class="html-italic">B. distachyon</span> roots infected with <span class="html-italic">N. crassa</span>. (<b>A</b>,<b>B</b>) Paraffin sections, 7 μm, stained with hematoxylin and eosin. Conidia outside the root (<b>A</b>,<b>B</b>). Hyphae (<b>*</b>) seen inside a few plant root cortical cells whereas the majority of root cortical cells do not appear to be infected (<b>A</b>). Hyphae (<b>*</b>) growing through the vascular bundle (<b>B</b>). (<b>C</b>,<b>D</b>) Epon sections, 1 μm, stained with Richardson’s solution. Hyphae (<b>*</b>) growing inside the vascular bundle of a moderately infected root with vascular elements preserved (<b>C</b>), and of a strongly infected root with disrupted vascular elements (<b>D</b>). Xylem elements can be recognized by secondary wall thickenings. Panels (<b>i</b>) display details of boxed areas. Asterisk (<b>*</b>): hypha.</p>
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<p>The TEM analysis of <span class="html-italic">B. distachyon</span> roots infected with <span class="html-italic">N. crassa</span>. Hyphae in epidermal cells (<b>A</b>,<b>B</b>), in cortical cells (<b>C</b>,<b>D</b>), in a moderately infected vascular bundle (<b>E</b>,<b>F</b>), and in a strongly infected vascular bundle (<b>G</b>–<b>J</b>). The plant cell cytoplasm/membrane (arrowheads) can be observed in infected cells and neighboring cells (<b>C</b>). Hyphae spread through the root by crossing plant cell walls (<b>D</b>,<b>F</b>). In a moderately infected root, plant vascular elements are largely preserved (<b>E</b>,<b>F</b>). In a strongly infected root, vascular elements are destroyed except for the xylem elements with secondary wall thickenings (<b>G</b>,<b>J</b>). Parallel, thin, black lines represent folds that were generated over these rigid cell walls during sectioning (<b>G</b>,<b>J</b>). Hyphae grow unrestricted (<b>H</b>) or inside the xylem vascular elements (<b>I</b>,<b>J</b>). The characteristic ultrastructure of fungal hyphae (<b>*</b>) includes the cell wall, septa (with pores) (arrows), and dense cytoplasm. Boxed areas (<b>A</b>,<b>E</b>,<b>G</b>,<b>J)</b> are shown as enlarged (<b>B</b>,<b>F</b>,<b>H</b>,<b>I</b>). Asterisk (<b>*</b>): hypha; white arrow: hyphal septum; black arrowhead: plant cell cytoplasm/membrane; Ep: epidermis; C: cortex; En: endodermis; Vb: vascular bundle; Cw: cell wall.</p>
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31 pages, 10023 KiB  
Article
A Study on a Compact Double Layer Sub-GHz Reflectarray Design Suitable for Wireless Power Transfer
by Romans Kusnins, Darja Cirjulina, Janis Eidaks, Kristaps Gailis, Ruslans Babajans, Anna Litvinenko, Deniss Kolosovs and Dmitrijs Pikulins
Electronics 2024, 13(14), 2754; https://doi.org/10.3390/electronics13142754 - 13 Jul 2024
Viewed by 381
Abstract
The paper presents a novel small-footprint varactor diode-based reconfigurable reflectarray (RRA) design and investigates its power reflection efficiency theoretically and experimentally in a real-life indoor environment. The surface is designed to operate at 865.5 MHz and is intended for simultaneous use with other [...] Read more.
The paper presents a novel small-footprint varactor diode-based reconfigurable reflectarray (RRA) design and investigates its power reflection efficiency theoretically and experimentally in a real-life indoor environment. The surface is designed to operate at 865.5 MHz and is intended for simultaneous use with other wireless power transfer (WPT) efficiency-improving techniques that have been recently reported in the literature. To the best of the authors’ knowledge, no RRA intended to improve the performance of antenna-based WPT systems operating in the sub-GHz range has been designed and studied both theoretically and experimentally so far. The proposed RRA is a two-layer structure. The top layer contains electronically tunable phase shifters for the local phase control of an incoming electromagnetic wave, while the other one is fully covered by metal to reduce the phase shifter size and RRA’s backscattering. Each phase shifter is a pair of diode-loaded 8-shaped metallic patches. Extensive numerical studies are conducted to ascertain a suitable set of RRA unit cell parameters that ensure both adequate phase agility and reflection uniformity for a given varactor parameter. The RRA design parameter finding procedure followed in this paper comprises several steps. First, the phase and amplitude responses of a virtual infinite double periodic RRA are computed using full-wave solver Ansys HFSS. Once the design parameters are found for a given set of physical constraints, the phase curve of the corresponding finite array is retrieved to estimate the side lobe level due to the finiteness of the RRA aperture. Then, a diode reactance combination is found for several different RRA reflection angles, and the corresponding RRA radiation pattern is computed. The numerical results show that the side lobe level and the deviation of the peak reflected power angles from the desired ones are more sensitive to the reflection coefficient magnitude uniformity than to the phase agility. Furthermore, it is found that for scanning angles less than 50°, satisfactory reflection efficiency can be achieved by using the classical reactance profile synthesis approach employing the generalized geometrical optics (GGO) approximation, which is in accord with the findings of other studies. Additionally, for large reflection angles, an alternative synthesis approach relying on the Floquet mode amplitude optimization is utilized to verify the maximum achievable efficiency of the proposed RRA at large angles. A prototype consisting of 36 elements is fabricated and measured to verify the proposed reflectarray design experimentally. The initial diode voltage combination is found by applying the GGO-based phase profile synthesis method to the experimentally obtained phase curve. Then, the voltage combination is optimized in real time based on power measurement. Finally, the radiation pattern of the prototype is acquired using a pair of identical 4-director printed Yagi antennas with a gain of 9.17 dBi and compared with the simulated. The calculated results are consistent with the measured ones. However, some discrepancies attributed to the adverse effects of biasing lines are observed. Full article
(This article belongs to the Special Issue Wireless Power Transfer System: Latest Advances and Prospects)
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<p>An illustration of an RRA-enhanced WPT system in an indoor environment. PB and SN stand for a power beacon and a sensor node, respectively.</p>
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<p>Ansys model of the RA unit cell.</p>
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<p>Ansys model of the RA unit cell (top view).</p>
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<p>The reflection coefficient phase as a function of varactor reactance calculated at different separations between the upper and the lower layers of infinity periodic RRA model.</p>
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<p>The reflection coefficient magnitude as a function of varactor reactance calculated at different separations between the upper and the lower layers of infinity periodic RRA model.</p>
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<p>The Ansys HFSS model of RA composed of 36 (18 × 2) FR-4 phase shifters, each consisting of two diode-loaded metallic 8-shaped patches (tunable surface resonators).</p>
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<p>The phase curves calculated at different diode reactance and inter-layer layer separation distances for an infinite RRA model and a finite model consisting of 36 (18 × 2) phase shifters.</p>
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<p>The farfield pattern in the azimuthal plane of the RA model with 18 × 2 varactor diode-loaded 8-shaped phase shifters computed at different diode reactance values in the range from 10 to 100 Ω when the inter-layer separation is 2 cm (<b>a</b>) and 4 cm (<b>b</b>).</p>
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<p>The calculated radiation pattern (Rx power in mW) in the azimuthal plane of the RRA consisting of 36 (18 × 2) phase shifters optimized for different reflection angles with <span class="html-italic">d =</span> 2 cm (<b>a</b>) and <span class="html-italic">d =</span> 3 cm (<b>b</b>).</p>
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<p>The calculated radiation pattern (Rx power in mW) in the azimuthal plane of the RRA consisting of 18 × 2 (<b>a</b>) and 36 × 2 (<b>b</b>) phase shifters with <span class="html-italic">d =</span> 4 cm configured for different reflection angles.</p>
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<p>The normalized calculated radiation pattern (received power in mW over the phase shifter number squared in the case of plane wave excitation with the electric field intensity of 1 V/m) in the azimuthal plane of the RRA optimized using the Floquet theory-based synthesis method for a desired reflection angle of 60° (<b>a</b>) and 80° (<b>b</b>).</p>
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<p>The experimental setup composed of the RRA under study and two Yagi antennas arranged for the measurement of phase curve (<b>a</b>) and for the RRA optimization for the desired reflection angles of 30° (<b>b</b>).</p>
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<p>The measurement setup comprising a custom made two stage RF signal power amplifier, digital oscilloscope Tektronix DPO72004C, and Rode–Schwartz SMR30 RF signal generator (<b>a</b>) and the experimental Yagi antenna arrangement intended for the measurement of the reflected power pattern of a metallic sheet (<b>b</b>).</p>
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<p>The calculated (solid line) and measured (dashed line) reflection coefficient phase against the diode bias voltage of a uniformly configured RRA consisting of 36 (18 × 2) phase shifters at different distances between the substrates.</p>
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<p>The calculated (red line) and measured (dashed black line) radiation pattern (Rx power in mW) in the azimuthal plane measured for the RRA consisting of 36 (18 × 2) 8-shaped phase shifters (red line) optimized for the desired angle of 30° (<b>a</b>) and 40° (<b>b</b>) and the flat metal sheet used as the reference reflector (blue line).</p>
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<p>The calculated (red line) and measured (dashed black line) radiation pattern (Rx power in mW) in the azimuthal plane measured for the RRA consisting of 36 (18 × 2) 8-shaped phase shifters (red line) optimized for the desired for the desired angle of 45° (<b>a</b>) and 50° (<b>b</b>) and the flat metal sheet used as the reference reflector (blue line).</p>
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10 pages, 6156 KiB  
Article
Accurate Detection and Analysis of Pore Defects in Laser Powder Bed Fusion WE43 Magnesium Alloys
by Zhengxing Men, Liang Wang, Xi Gao, Wen Chen, Chen Ji, Ziche Li and Kun Li
Micromachines 2024, 15(7), 909; https://doi.org/10.3390/mi15070909 - 12 Jul 2024
Viewed by 478
Abstract
To explore the size, morphology, and distribution patterns of internal pore defects in WE43 magnesium alloy formed by laser powder bed fusion (LPBF), as well as their impact on its mechanical properties, computer tomography (CT), metallographic microscopy, and scanning electron microscopy were used [...] Read more.
To explore the size, morphology, and distribution patterns of internal pore defects in WE43 magnesium alloy formed by laser powder bed fusion (LPBF), as well as their impact on its mechanical properties, computer tomography (CT), metallographic microscopy, and scanning electron microscopy were used to observe the material’s microstructure and the morphology of tensile test fractures. The study revealed that a large number of randomly distributed non-circular pore defects exist internally in the LPBF-formed WE43 magnesium alloy, with a defect volume fraction of 0.16%. Approximately 80% of the defects had equivalent diameters concentrated in the range of 10∼40 μm, and 56.2% of the defects had sphericity values between 0.65∼0.7 μm, with the maximum defect equivalent diameter being 122 μm. There were a few spherical pores around 20 μm in diameter in the specimens, and unfused powder particles were found in pore defects near the edges of the parts. Under the test conditions, the fusion pool structure of LPBF-formed WE43 magnesium alloy resembled a semi-elliptical shape with a height of around 66 μm, capable of fusion three layers of powder material in a single pass. Columnar grains formed at the edge of individual fusion pools, while the central area exhibited equiaxed grains. The “scale-like pattern” formed by overlapping fusion pool structures resulted in the microstructure of LPBF-formed WE43 magnesium alloy mainly consisting of fine equiaxed grains with a size of 2.5 μm and columnar grains distributed in a band-like manner. Full article
(This article belongs to the Special Issue Optical and Laser Material Processing)
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<p>WE43 magnesium alloy tensile specimen. (<b>a</b>) Size of WE43 tensile sample formed by LPED. (<b>b</b>) Sample physical object. (<b>c</b>) Mesh partitioning for finite element analysis.</p>
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<p>CT inspection results of LPBF-formed WE43 magnesium alloy. (<b>a</b>) Pore defects with an equivalent diameter of 10 <math display="inline"><semantics> <mi mathvariant="sans-serif">μ</mi> </semantics></math>m and larger. (<b>b</b>) Pore defects with an equivalent diameter in the range of 77 <math display="inline"><semantics> <mi mathvariant="sans-serif">μ</mi> </semantics></math>m to 122 <math display="inline"><semantics> <mi mathvariant="sans-serif">μ</mi> </semantics></math>m. (<b>c</b>) Pore defects with an equivalent diameter of 122.235 <math display="inline"><semantics> <mi mathvariant="sans-serif">μ</mi> </semantics></math>m. Its sphericity is measured at 0.6, resembling a horn-like morphology in (<b>d</b>).</p>
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<p>XY Cross-sectional CT Inspection Results of Tensile Specimen. (<b>a</b>) 2.37 mm from the bottom surface. (<b>b</b>) 9.54 mm from the bottom surface. (<b>c</b>) 15.43 mm from the bottom surface. (<b>d</b>) 19.14 mm from the bottom surface.</p>
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<p>ZX and YZ cross-sectional CT inspection results of tensile specimen. (<b>a</b>) Parallel to the ZX plane and 0.58 mm away from the side. (<b>b</b>) Parallel to the ZX plane and 1.58 mm away from the side. (<b>c</b>) Parallel to the ZY plane and 1.12 mm away from the side. (<b>d</b>) Parallel to the ZY plane and 2.44 mm away from the side.</p>
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<p>Distribution and normal distribution curve of defect sizes in WE43 magnesium alloy.</p>
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<p>Sphericity and normal distribution curve distribution of defects in WE43 magnesium alloy.</p>
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<p>Appearance of WE43 prepared by LPBF. (<b>a</b>) Specific microstructural formations along the longitudinal cross-section of the part. (<b>b</b>,<b>e</b>)Isolated defects. (<b>c</b>,<b>d</b>) Continuous defects.</p>
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<p>The outer surface Fusion pool structure of WE43 prepared by LPBF.</p>
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<p>High magnification morphology of WE43 prepared by LPBF. (<b>a</b>) Cross sectional microstructure diagram of WE43 magnesium alloy formed by LPBF after etching. (<b>b</b>) Longitudinal cross-sectional microstructure diagram of the edge of WE43 magnesium alloy specimen formed by LPBF.</p>
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<p>Room temperature tensile curve of LPBF-formed WE43. (<b>a</b>) The room temperature tensile curve of LPBF-formed WE43 magnesium alloy. (<b>b</b>) Stress–strain curve of LPBF formed D-WE43 magnesium alloy. (<b>c</b>) Neck contraction diagram of the fracture area. (<b>d</b>,<b>e</b>) Fracture surface of WE43 magnesium alloy.</p>
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18 pages, 5528 KiB  
Article
Fabrication of Cu2O/CuO Nanowires by One-Step Thermal Oxidation of Flexible Copper Mesh for Supercapacitor Applications
by Mina-Ionela Morariu (Popescu), Mircea Nicolaescu, Iosif Hulka, Narcis Duţeanu, Corina Orha, Carmen Lăzău and Cornelia Bandas
Batteries 2024, 10(7), 246; https://doi.org/10.3390/batteries10070246 - 10 Jul 2024
Viewed by 814
Abstract
This study focuses on the growth of Cu2O/CuO nanowires by one-step thermal oxidation using a flexible copper mesh at oxidation temperatures in the range of 300 to 600 °C in a controlled atmosphere of mixed-flow Ar and O2 gases. Thermal [...] Read more.
This study focuses on the growth of Cu2O/CuO nanowires by one-step thermal oxidation using a flexible copper mesh at oxidation temperatures in the range of 300 to 600 °C in a controlled atmosphere of mixed-flow Ar and O2 gases. Thermal oxidation is one of the simplest used methods to obtain nanowires on a metal surface, offering advantages such as low production costs and the ability to produce metal oxides on a large scale without the use of hazardous chemical compounds. The growth of metal oxides on a conductive substrate, forming metal/oxide structures, has proven to be an effective method for enhancing charge-transfer efficiency. The as-synthesized Cu/Cu2O/CuO (Nw) electrodes were structurally and morphologically characterized using techniques such as XRD and SEM/EDX analysis to investigate the structure modification and morphologies of the materials. The supercapacitor properties of the as-developed Cu/Cu2O/CuO (Nw) electrodes were then examined using cyclic voltammetry (CV), galvanostatic charge–discharge (GCD) measurements, and electrochemical impedance spectroscopy (EIS). The CV curves show that the Cu/Cu2O/CuO (Nw) structure acts as a positive electrode, and, at a scan rate of 5 mV s −1, the highest capacitance values reached 26.158 mF cm−2 for the electrode oxidized at a temperature of 300 °C. The assessment of the flexibility of the electrodes was performed at various bending angles, including 0°, 45°, 90°, 135°, and 180°. The GCD analysis revealed a maximum specific capacitance of 21.198 mF cm−2 at a low power density of 0.5 mA cm−2 for the oxidation temperature of 300 °C. The cycle life assessment of the all of the as-obtained Cu/Cu2O/CuO (Nw) electrodes over 500 cycles was performed by GCD analysis, which confirmed their electrochemical stability. Full article
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<p>Schematic diagram of the synthesis protocol for the development of the Cu/Cu<sub>2</sub>O/CuO (Nw) electrode.</p>
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<p>XRD spectra of the as-obtained Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes at different oxidation temperatures.</p>
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<p>SEM morphologies for raw Cu mesh (<b>a</b>) and for Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes oxidized at temperatures of 300 °C (<b>b</b>), 400 °C (<b>c</b>), 500 °C (<b>d</b>), and 600 °C (<b>e</b>).</p>
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<p>SEM morphologies for raw Cu mesh (<b>a</b>) and for Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes oxidized at temperatures of 300 °C (<b>b</b>), 400 °C (<b>c</b>), 500 °C (<b>d</b>), and 600 °C (<b>e</b>).</p>
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<p>Cyclic voltammograms recorded for Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes obtained by thermal oxidation at 300 °C (<b>a</b>), 400 °C (<b>b</b>), 500 °C (<b>c</b>), and 600 °C (<b>d</b>). Plots of specific capacitance vs. potential scan rate of the electrodes (<b>e</b>).</p>
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<p>GCD curves of Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes obtained by thermal oxidation at 300 °C (<b>a</b>), 400 °C (<b>b</b>), 500 °C (<b>c</b>), and 600 °C (<b>d</b>). Specific capacitance vs. current density for all as-obtained electrodes (<b>e</b>).</p>
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<p>(<b>a</b>) GCD curves in accordance with cycling stability and (<b>b</b>) specific capacitance at 500 cycles of the as-obtained Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes at a current density of 8 mA cm<sup>−2</sup>.</p>
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<p>(<b>a</b>) GCD curves in accordance with cycling stability and (<b>b</b>) specific capacitance at 500 cycles of the as-obtained Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes at a current density of 8 mA cm<sup>−2</sup>.</p>
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<p>Nyquist plots of all as-obtained Cu/Cu<sub>2</sub>O/CuO (Nw) electrodes (<b>a</b>). Simulation of the equivalent circuit fitting of the electrodes (<b>b</b>).</p>
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11 pages, 3049 KiB  
Article
Advancing Lithium-Ion Batteries’ Electrochemical Performance: Ultrathin Alumina Coating on Li(Ni0.8Co0.1Mn0.1)O2 Cathode Materials
by Mehdi Ahangari, Fan Xia, Benedek Szalai, Meng Zhou and Hongmei Luo
Micromachines 2024, 15(7), 894; https://doi.org/10.3390/mi15070894 (registering DOI) - 9 Jul 2024
Cited by 1 | Viewed by 557
Abstract
Ni-rich Li(NixCoyMnz)O2 (x ≥ 0.8)-layered oxide materials are highly promising as cathode materials for high-energy-density lithium-ion batteries in electric and hybrid vehicles. However, their tendency to undergo side reactions with electrolytes and their structural instability during [...] Read more.
Ni-rich Li(NixCoyMnz)O2 (x ≥ 0.8)-layered oxide materials are highly promising as cathode materials for high-energy-density lithium-ion batteries in electric and hybrid vehicles. However, their tendency to undergo side reactions with electrolytes and their structural instability during cyclic lithiation/delithiation impairs their electrochemical cycling performance, posing challenges for large-scale applications. This paper explores the application of an Al2O3 coating using an atomic layer deposition (ALD) system on Ni-enriched Li(Ni0.8Co0.1Mn0.1)O2 (NCM811) cathode material. Characterization techniques, including X-ray diffraction, scanning electron microscopy, and transmission electron microscopy, were used to assess the impact of alumina coating on the morphology and crystal structure of NCM811. The results confirmed that an ultrathin Al2O3 coating was achieved without altering the microstructure and lattice structure of NCM811. The alumina-coated NCM811 exhibited improved cycling stability and capacity retention in the voltage range of 2.8–4.5 V at a 1 C rate. Specifically, the capacity retention of the modified NCM811 was 5%, 9.11%, and 11.28% higher than the pristine material at operating voltages of 4.3, 4.4, and 4.5 V, respectively. This enhanced performance is attributed to reduced electrode–electrolyte interaction, leading to fewer side reactions and improved structural stability. Thus, NCM811@Al2O3 with this coating process emerges as a highly attractive candidate for high-capacity lithium-ion battery cathode materials. Full article
(This article belongs to the Special Issue Energy Conversion Materials/Devices and Their Applications)
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<p>XRD patterns comparing the (a) pristine and (b) NCM811 surface modified with Al<sub>2</sub>O<sub>3</sub>.</p>
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<p>SEM images showing (<b>a</b>) pristine and (<b>b</b>) NCM811 coated with Al<sub>2</sub>O<sub>3</sub>, along with EDS-mapping of (<b>c</b>) pristine NCM811 and (<b>d</b>) Al<sub>2</sub>O<sub>3</sub>-coated NCM811 particles. Additionally, TEM images depicting the Al<sub>2</sub>O<sub>3</sub>-coated NCM811 particle are shown in (<b>e</b>).</p>
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<p>Electrochemical properties of bare and Al<sub>2</sub>O<sub>3</sub>-coated NCM811 over 150 cycles (1 C) at 4.3, 4.4, and 4.5 upper cutoff voltages. The upper figures compare the cycling stability of the samples, while the lower ones illustrate the voltage fading after 150 cycles.</p>
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<p>Rate capability for pristine and NCM811@Al<sub>2</sub>O<sub>3</sub> at different cutoff voltages.</p>
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<p>EIS curves of charged bare and Al<sub>2</sub>O<sub>3</sub>-coated NCM811 at 4.3–4.5 voltage range before cycling and after 150 cycles.</p>
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<p>CV curves of (<b>a</b>) pristine and (<b>b</b>) Al<sub>2</sub>O<sub>3</sub>-coated NCM811 at a scan rate of 0.1 mV s<sup>−1</sup> within a 2.8–4.6 V voltage range.</p>
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19 pages, 4509 KiB  
Article
Impact of Anthropogenic Activities on Sedimentary Records in the Lingdingyang Estuary of the Pearl River Delta, China
by Dezheng Liu, Yitong Lin, Tao Zhang, Enmao Huang, Zhiyuan Zhu and Liangwen Jia
J. Mar. Sci. Eng. 2024, 12(7), 1139; https://doi.org/10.3390/jmse12071139 - 6 Jul 2024
Viewed by 529
Abstract
High-intensity anthropogenic activities have greatly altered the estuarine-shelf depositional processes of sediments, and the intensity and frequency of the impacts of human interventions have far exceeded the natural development of estuarine systems. Since the reform and opening up, human activities such as dams, [...] Read more.
High-intensity anthropogenic activities have greatly altered the estuarine-shelf depositional processes of sediments, and the intensity and frequency of the impacts of human interventions have far exceeded the natural development of estuarine systems. Since the reform and opening up, human activities such as dams, sand mining, channel dredging, and reclamation have already caused anomalous changes in the dynamical–sedimentary–geomorphological processes of the Lingdingyang Estuary (LE). Analyzing the impact of high-intensity anthropogenic activities on sedimentary processes and the hydrodynamic environment through sedimentary records can provide a scientific basis for predicting the evolution of the estuary and the sustainable development of the Guangdong–Hongkong–Macao Greater Bay Area. The aims of this study are to reveal the impact of varying intensity human activities across different periods on depositional pattern and conduct a preliminary investigation into the spatial differences in sedimentary characteristic attributed to human activities. Two cores (LD11 and LD13) located in the LE were selected for continuous scanning of high-resolution XRF, grain size, and 210Pbex dating tests, and scrutinized with the previous studies of the historical process of human activities in the LE. The results show the following: (1) The abrupt alterations in 210Pbex, geochemical indices, and grain size in LD13 happened in close proximity to the 95 cm layer, suggesting a shift in the sedimentary environment during 1994. (2) In the context of the continuous reduction in water and sediment flux into the LE after 1994, the large-scale and high-intensity human activities like sand mining, channel dredging, and reclamation are responsible for the sedimentation rate increase rather than decrease, the coarsening of sediment fractions, the frequent fluctuations in Zr/Rb, Zr/Al, Sr/Fe, and Sr/Al ratios, and the increase in anomalous extremes. (3) Sedimentary records found in locations varying in anthropogenic intensities differ greatly. Compared with the nearshore siltation area, the grain size composition in the channel area is noticeably coarser and exhibits a wider range of grain size variations. The 210Pbex is strongly perturbed and the vertical distribution is disturbed; the phenomenon of multiple inversions from the surface downwards is shown, making it impossible to carry out sedimentation rate and dating analysis, and the geochemical indicators have changed drastically without any obvious pattern. The evidence of the human activities can be retrieved in the sedimentary record of the estuary and provide a different angle to examine the impacts of the human activities. Full article
(This article belongs to the Section Coastal Engineering)
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<p>(<b>a</b>) A map of the Pearl River basin. (<b>b</b>) Location map of four outlets (Humen, Jiaomen, Hongqili, and Hengmen), three shoals (west shoals, middle shoals, and east shoals), main shipping lane (Lingding waterway, Fanshi waterway, and Tonggu waterway), and sampling sites (LD11 and LD13). (<b>c</b>) Gross domestic product of the LE coastal cities (data are available at <a href="http://www.dsec.gov.mo" target="_blank">www.dsec.gov.mo</a> (accessed on 1 May 2024) and <a href="http://stats.gd.gov.cn" target="_blank">stats.gd.gov.cn</a> (accessed on 1 May 2024)).</p>
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<p>Photographs of cores LD11 and LD13 (units: cm). Core LD11 measures 167 cm in length, while LD13 measures 185 cm.</p>
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<p>(<b>a</b>) Vertical distribution of <sup>210</sup>Pb<sub>ex</sub> in core LD11 (Red dots is excess <sup>210</sup>Pb radioactivity). (<b>b</b>) Vertical distribution of <sup>210</sup>Pb<sub>ex</sub> and exponential fitting between depth (<span class="html-italic">Y</span> axis: cm) and <sup>210</sup>Pb<sub>ex</sub> (<span class="html-italic">X</span> axis: dpm·g<sup>−1</sup>) in core LD13 (Yellow dots is excess <sup>210</sup>Pb radioactivity in the upper section; Red dots is excess <sup>210</sup>Pb radioactivity in the lower section; Black dashed lines is the fitting curve). (<b>c</b>) The depth–age framework of LD13 based on CIC and CRS model.</p>
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<p>Vertical variation of grain size content in cores LD11 (<b>left</b>) and LD13 (<b>right</b>), and the traces of human disturbance in the sediment of core LD11 can be observed (Figure. A).</p>
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<p>Sensitive grain size curves, variations in content of grain size, and &lt;6.29 Φ components of core LD13 are as follows: There are two peak values of standard deviation at 4.64 Φ and 7.77 Φ, respectively; 6.29 Φ is the separation point between two sensitive grain sizes. The 95 cm layer shows significant changes in particle size distribution. The content of the &lt;6.29 Φ component decreases from the top to the bottom of the core (the red line represents the average contents of the &lt;6.29 Φ component).</p>
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<p>Variation of the element ratios over time in core LD11 (red dotted line is the average value).</p>
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<p>Variation of the element ratios over time in core LD13 (red dotted line is the average value).</p>
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<p>Annual variation of water discharge and sediment load from Pearl River to the estuary since the 1950s, as measured at Gaoyao, Shijiao, and Boluo stations.</p>
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<p>Schematic diagram of reclamation, sand mining, and waterway dredging in the LDB during 1972–2017 (HuM: Humen, JM: Jiaomen, HQL: Hongqili, HM: Hengmen).</p>
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<p>The main human activities in the LE in the past 70 years.</p>
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25 pages, 20276 KiB  
Article
Powder Bed Fusion–Laser Beam of IN939: The Effect of Process Parameters on the Relative Density, Defect Formation, Surface Roughness and Microstructure
by Merve Nur Doğu, Muhannad Ahmed Obeidi, Hengfeng Gu, Chong Teng and Dermot Brabazon
Materials 2024, 17(13), 3324; https://doi.org/10.3390/ma17133324 - 5 Jul 2024
Viewed by 917
Abstract
This study investigates the effects of process parameters in the powder bed fusion–laser beam (PBF-LB) process on IN939 samples. The parameters examined include laser power (160, 180, and 200 W), laser scanning speed (400, 800, and 1200 mm/s), and hatch distance (50, 80, [...] Read more.
This study investigates the effects of process parameters in the powder bed fusion–laser beam (PBF-LB) process on IN939 samples. The parameters examined include laser power (160, 180, and 200 W), laser scanning speed (400, 800, and 1200 mm/s), and hatch distance (50, 80, and 110 μm). The study focuses on how these parameters affect surface roughness, relative density, defect formation, and the microstructure of the samples. Surface roughness analysis revealed that the average surface roughness (Sa) values of the sample ranged from 4.6 μm to 9.5 μm, while the average height difference (Sz) varied from 78.7 μm to 176.7 μm. Furthermore, increasing the hatch distance from 50 μm to 110 μm while maintaining constant laser power and scanning speed led to a decrease in surface roughness. Relative density analysis indicated that the highest relative density was 99.35%, and the lowest was 93.56%. Additionally, the average porosity values were calculated, with the lowest being 0.06% and the highest reaching 9.18%. Although some samples had identical average porosity values, they differed in porosity/mm2 and average Feret size. Variations in relative density and average porosity were noted in samples with the same volumetric energy density (VED) due to different process parameters. High VED led to large, irregular pores in several samples. Microcracks, less than 50 μm in length, were present, indicating solidification cracks. The microstructural analysis of the XZ planes revealed arc-shaped melt pools, columnar elongated grains aligned with the build direction, and cellular structures with columnar dendrites. This study provides insights for optimizing PBF-LB process parameters to enhance the quality of IN939 components. Full article
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<p>Images of the build plate after fabrication and a schematic of the as-built IN939 samples. The XZ plane (parallel to the build direction) and the XY plane (perpendicular to the build direction) are indicated with arrows and dots, respectively.</p>
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<p>Surface roughness profiles of the selected as-built IN939 samples (samples 1, 8, 17, and 21).</p>
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<p>RSM graphs of the surface roughness (μm) versus the different input processing parameters. Hatch distance: (<b>a</b>) 50 μm, (<b>b</b>) 80 μm and (<b>c</b>) 110 μm.</p>
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<p>RSM graphs of the relative density (%) versus the different input processing parameters. Hatch distance: (<b>a</b>) 50 μm, (<b>b</b>) 80 μm and (<b>c</b>) 110 μm.</p>
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<p>The as-polished optical micrographs of as-built samples (1–9) in the XZ plane (parallel to the build direction). Porosity (%) values are indicated on the micrographs (hatch distance: 50 μm).</p>
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<p>The as-polished optical micrographs of as-built samples (10–18) in the XZ plane (parallel to the build direction). Porosity (%) values are indicated on the micrographs (hatch distance: 80 μm).</p>
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<p>The as-polished optical micrographs of as-built samples (19–27) in the XZ plane (parallel to the build direction). Porosity (%) values are indicated on the micrographs (hatch distance: 110 μm).</p>
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<p>Optical micrographs of the XZ planes of the selected as-built samples (1, 8, 11, 12, 14, 17, 21, 25, and 26).</p>
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<p>SEM images of the XZ planes of the selected as-built samples (1, 8, 14, 17, and 26), along with EDS results of the MC-type carbides.</p>
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<p>Optical images of the XZ planes of the as-built IN939 samples (1–27).</p>
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<p>(<b>a</b>) Relative density (%) and (<b>b</b>) average porosity (%) versus VED (J/mm<sup>3</sup>) graphs of the as-built samples.</p>
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<p>The as-polished optical micrographs of as-built samples (1–27) in the XY plane (perpendicular to the build direction). Porosity (%) values are indicated on the micrographs.</p>
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<p>Optical micrographs of the XZ planes of the selected as-built samples (1, 8, 14, 17, and 26).</p>
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14 pages, 2562 KiB  
Article
Utilizing Date Palm Leaf Biochar for Simultaneous Adsorption of Pb(II) and Iodine from Aqueous Solutions
by Essam R. I. Mahmoud, Hesham M. Aly, Noura A. Hassan, Abdulrahman Aljabri, Asim Laeeq Khan and Hashem F. El-Labban
Processes 2024, 12(7), 1370; https://doi.org/10.3390/pr12071370 - 1 Jul 2024
Viewed by 612
Abstract
This study addresses the environmental and health hazards posed by Pb(II) and iodine, two significant contaminants. The objective was to explore the adsorption of these substances from aqueous solutions using biochar derived from the leaf midribs of the date palm through a slow [...] Read more.
This study addresses the environmental and health hazards posed by Pb(II) and iodine, two significant contaminants. The objective was to explore the adsorption of these substances from aqueous solutions using biochar derived from the leaf midribs of the date palm through a slow pyrolysis process. The pyrolysis was conducted in two stages within a vacuum furnace: initially at 300 °C for 1 h followed by overnight cooling, and then at 600 °C with a similar cooling process. The resulting biochar was characterized for its microstructural features and functional groups using scanning electron microscopy (SEM) and Fourier transform infrared (FT-IR) spectroscopy. It exhibited a porous structure with large numbers of pores (20 to 50 μm in size) and functional groups including O-H, C-H, and C=C, which are integral to its adsorption capabilities. For the adsorption studies, a 100 ppm Pb(II) ion solution was treated with varying amounts of biochar (20, 40, 60, and 80 mg) for 24 h. In parallel, iodine adsorption was tested, with biochar quantities ranging from 0.1 to 0.4 g/50 mL. Both treatments were followed by filtration and analysis using atomic absorption spectroscopy to determine the remaining concentrations of Pb(II) and iodine. The study also explored the effect of varying incubation periods (up to 30 h) on iodine adsorption. The results were significant; 100% adsorption of Pb(II) was achieved with the addition of 60 mg of biochar per 10 mL of solution. In contrast, for iodine, a maximum adsorption of 39.7% was observed with 30 mg or 40 mg of biochar per 50 mL. These findings demonstrate the potential of date palm-derived biochar as an effective and sustainable material for the removal of Pb(II) and iodine from contaminated water, offering valuable insights for environmental remediation strategies. Full article
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<p>SEM images of the microstructure of the biochar surface at two different zones: (<b>a</b>) anterior vessels, and (<b>b</b>) lateral vessels.</p>
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<p>Electron dispersive X-ray (EDX) image of the biochar after Pb(II) adsorption.</p>
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<p>FTIR spectra of biochar before Pb(II) adsorption.</p>
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<p>Calibration curve of Pb(II).</p>
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<p>Adsorption of iodine on biochar at different incubation times.</p>
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