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16 pages, 7491 KiB  
Article
Effects of Surface Treatment on Adhesive Performance of Composite-to-Composite and Composite-to-Metal Joints
by Nikhil Paranjpe, Md. Nizam Uddin, Akm Samsur Rahman and Ramazan Asmatulu
Processes 2024, 12(12), 2623; https://doi.org/10.3390/pr12122623 - 21 Nov 2024
Abstract
This study deals with the long-running challenge of joining similar and dissimilar materials using composite-to-composite and composite-to-metal joints. This research was conducted to evaluate the effects of surface morphology and surface treatments on the mechanical performance of adhesively bonded joints used for the [...] Read more.
This study deals with the long-running challenge of joining similar and dissimilar materials using composite-to-composite and composite-to-metal joints. This research was conducted to evaluate the effects of surface morphology and surface treatments on the mechanical performance of adhesively bonded joints used for the aircraft industry. A two-segment, commercially available, toughened epoxy was chosen as the adhesive. Unidirectional carbon fiber prepreg and aluminum 2021-T3 alloys were chosen for the composite and metal panels, respectively. Surface treatment of the metal included corrosion elimination followed by a passive surface coating of Alodine®. A combination of surface treatment methods was used for the composite and metal specimens, including detergent cleaning, plasma exposure, and sandblasting. The shear strength of the single-lap adhesive joint was evaluated according to the ASTM D1002. Ultraviolet (UV) and plasma exposure effects were studied by measuring the water contact angles. The test results showed that the aluminum adherent treated with sandblasting, detergent, and UV irradiation resulted in the strongest adhesive bonding of the composite-to-composite panels, while the composite-to-metal sample cleaned only with detergent resulted in the least bonding strength. The failure strain of the composite-to-composite bonding was reduced by approximately 50% with only sandblasting. However, extended treatment did not introduce additional brittleness in the adhesive joint. The bonding strength of the composite-to-composite panel improved by approximately 35% with plasma treatment alone because of the better surface functionalization and bonding strength. In the composite-to-aluminum bonding process, exposing the aluminum surface to UV resulted in 30% more joint strength compared to the Alodine® coating, which suggests the origination of higher orders of magnitude of covalent groups from the surface. A comparison with published results found that the joint strengths in both similar and dissimilar specimens are higher than most other results. Detailed observations and surface analysis studies showed that the composite-to-composite bonding mainly failed due to adhesive and cohesive failures; however, failure of the composite-to-aluminum bonding was heterogeneous, where adhesive failure occurred on the aluminum side and substrate failure occurred on the composite side. Full article
(This article belongs to the Special Issue Development and Characterization of Advanced Polymer Nanocomposites)
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Figure 1

Figure 1
<p>Schematic for a plasma treatment process [<a href="#B24-processes-12-02623" class="html-bibr">24</a>].</p>
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<p>Composite-to-composite and composite-to-aluminum single-lap joint process.</p>
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<p>Effect of plasma treatment on wettability of composite surfaces before and after sandpapering.</p>
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<p>Effects of various surface and plasma treatments on wettability of aluminum alloy surface.</p>
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<p>Stress–strain diagram of composite-to-composite adhesive bonding with sandpaper at various plasma treatment times.</p>
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<p>Joint strength of plasma-treated composite-to-composite surface with different surface preparations (CT—detergent cleaned, ST—sand treatment).</p>
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<p>Joint strength of composite-to-aluminum surface with different surface preparations. (CT—detergent cleaned, ST—sand treatment, PT—plasma treatment, Coat—Alodine<sup>®</sup>-coated, UV—UV treatment).</p>
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<p>Lap shear fracture surfaces: (<b>a</b>,<b>b</b>) composite-to-composite joints and (<b>c</b>,<b>d</b>) composite-to-aluminum joints.</p>
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<p>Demonstration of lap joint failure modes under axial tensile load: (<b>a</b>–<b>c</b>) composite-to-aluminum and (<b>d</b>,<b>e</b>) composite-to-composite [<a href="#B43-processes-12-02623" class="html-bibr">43</a>,<a href="#B44-processes-12-02623" class="html-bibr">44</a>].</p>
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20 pages, 4201 KiB  
Article
Impact of Particle Size and Sintering Temperature on Calcium Phosphate Gyroid Structure Scaffolds for Bone Tissue Engineering
by Romina Haydeé Aspera-Werz, Guanqiao Chen, Lea Schilonka, Islam Bouakaz, Catherine Bronne, Elisabeth Cobraiville, Grégory Nolens and Andreas Nussler
J. Funct. Biomater. 2024, 15(12), 355; https://doi.org/10.3390/jfb15120355 - 21 Nov 2024
Abstract
Due to the chemical composition and structure of the target tissue, autologous bone grafting remains the gold standard for orthopedic applications worldwide. However, ongoing advancements in alternative grafting materials show that 3D-printed synthetic biomaterials offer many advantages. For instance, they provide high availability, [...] Read more.
Due to the chemical composition and structure of the target tissue, autologous bone grafting remains the gold standard for orthopedic applications worldwide. However, ongoing advancements in alternative grafting materials show that 3D-printed synthetic biomaterials offer many advantages. For instance, they provide high availability, have low clinical limitations, and can be designed with a chemical composition and structure comparable to the target tissue. This study aimed to compare the influences of particle size and sintering temperature on the mechanical properties and biocompatibility of calcium phosphate (CaP) gyroid scaffolds. CaP gyroid scaffolds were fabricated by 3D printing using powders with the same chemical composition but different particle sizes and sintering temperatures. The physicochemical characterization of the scaffolds was performed using X-ray diffractometry, scanning electron microscopy, and microtomography analyses. The immortalized human mesenchymal stem cell line SCP-1 (osteoblast-like cells) and osteoclast-like cells (THP-1 cells) were seeded on the scaffolds as mono- or co-cultures. Bone cell attachment, number of live cells, and functionality were assessed at different time points over a period of 21 days. Improvements in mechanical properties were observed for scaffolds fabricated with narrow-particle-size-distribution powder. The physicochemical analysis showed that the microstructure varied with sintering temperature and that narrow particle size distribution resulted in smaller micropores and a smoother surface. Viable osteoblast- and osteoclast-like cells were observed for all scaffolds tested, but scaffolds produced with a smaller particle size distribution showed less attachment of osteoblast-like cells. Interestingly, low attachment of osteoclast-like cells was observed for all scaffolds regardless of surface roughness. Although bone cell adhesion was lower in scaffolds made with powder containing smaller particle sizes, the long-term function of osteoblast-like and osteoclast-like cells was superior in scaffolds with improved mechanical properties. Full article
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Figure 1
<p>Scaffold with cylindrical shape and gyroid structure. (<b>a</b>) Top view. (<b>b</b>) Side view.</p>
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<p>Powder composition determined by X-ray diffractometry (XRD). Representative XRD curve for (<b>a</b>) powder A and (<b>b</b>) powder B.</p>
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<p>Mechanical characterization of the three scaffolds tested. (<b>a</b>) Maximum force, (<b>b</b>) maximum stress, (<b>c</b>) displacements at maximum load, and (<b>d</b>) flexural strength were analyzed on scaffolds generated with powder A sintering at 1230 °C [Scaffold A] or powder B sintering at 1250 °C and 1210 °C [scaffolds B<sub>I</sub> and B<sub>II</sub>, respectively]. The data are presented as the mean, standard error of the mean, and all data points. Data were analyzed by the Kruskal–Wallis test followed by Dunn’s multiple comparisons. <span class="html-italic">p</span>-values are classified as * <span class="html-italic">p</span> &lt; 0.05; *** <span class="html-italic">p</span> &lt; 0.001; and **** <span class="html-italic">p</span> &lt; 0.0001 for comparison between scaffold B and scaffold A and as # <span class="html-italic">p</span> &lt; 0.05 for comparison within scaffold B.</p>
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<p>Surface topographies of the three scaffolds analyzed by scanning electron microscopy (SEM). (<b>a</b>) Scaffold generated with powder A and sintering at 1230 °C. (<b>b</b>) Scaffold generated with powder B and sintering at 1250 °C. (<b>c</b>) Scaffold generated with powder B and sintering at 1210 °C (scale bar 10 µm).</p>
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<p>SCP-1 cell attachment, number of live cells, and proliferation on three scaffolds tested. SCP-1 cells were seeded and cultured on scaffolds A, B<sub>I</sub>, and B<sub>II</sub> for 21 days. (<b>a</b>) Attached SCP-1 cells on scaffolds compared to cultured polystyrene. Number of live SCP-1 cells were analyzed after 24 h, 48 h, 7 days, 14 days, and 21 days by total DNA levels (<b>b</b>) and visualized by esterase activity (<b>c</b>) using calcein-AM (green) and nuclear staining using Hoechst 33342 (blue) (scale bar 2000 µm). Each measure was conducted at least three independent times in triplicate. The data are presented as the mean, standard error of the mean, and all data points. Data were analyzed by the Kruskal–Wallis test followed by Dunn’s multiple comparisons (<b>a</b>) or a two-way analysis of variance test followed by Tukey’s multiple comparisons (<b>b</b>). <span class="html-italic">p</span>-values are classified as ** <span class="html-italic">p</span> &lt; 0.01; *** <span class="html-italic">p</span> &lt; 0.001; and **** <span class="html-italic">p</span> &lt; 0.0001 for comparison between scaffold B and scaffold A and as ## <span class="html-italic">p</span> &lt; 0.01; ### <span class="html-italic">p</span> &lt; 0.001; and #### <span class="html-italic">p</span> &lt; 0.0001 for comparison within scaffold B.</p>
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<p>SCP-1 osteogenic differentiation potential on three scaffolds tested. SCP-1 cells were seeded and cultured under osteogenic condition on scaffolds A, BI, and BII for 21 days. (<b>a</b>) Metabolic activity of SCP-1 cells were analyzed after 24 h, 48 h, 7 days, 14 days, and 21 days by mitochondrial activity as relative fluorescence units (RFU). (<b>b</b>) Alkaline phosphatase (AP) activity normalized to DNA of SCP-1 cells were analyzed after 7 days, 14 days, and 21 days as relative absorbance units (RAU). (<b>c</b>) Procollagen type I N-propeptide (PINP) supernatant levels were determined after 21-day osteogenic culture. Each measure was conducted at least three independent times in duplicate. The data are presented as the mean, standard error of the mean, and all data points. Data were analyzed by a two-way analysis of variance test followed by Tukey’s multiple comparisons. <span class="html-italic">p</span>-values are classified as * <span class="html-italic">p</span> &lt; 0.05; ** <span class="html-italic">p</span> &lt; 0.01; and **** <span class="html-italic">p</span> &lt; 0.0001 for comparison between scaffold B and scaffold A and as # <span class="html-italic">p</span> &lt; 0.05; ## <span class="html-italic">p</span> &lt; 0.01; ### <span class="html-italic">p</span> &lt; 0.001; and #### <span class="html-italic">p</span> &lt; 0.0001 for comparison within scaffold B.</p>
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<p>THP-1 cell attachment and number of live cells on three scaffolds tested. THP-1 cells were seeded and cultured on scaffolds A, BI, and BII for 24 h. (<b>a</b>) Attached SCP-1 cells on scaffolds compared to cultured polystyrene. Number of live THP-1 cells were visualized after 24 h by esterase activity (<b>b</b>) using calcein-AM (green) and nuclear staining using Hoechst 33342 (blue) (scale bar 2000 µm). Each measure was conducted at least three independent times in triplicate. The data are presented as the mean, standard error of the mean, and all data points. Data were analyzed by the Kruskal–Wallis test followed by Dunn’s multiple comparisons. <span class="html-italic">p</span>-values are classified as **** <span class="html-italic">p</span> &lt; 0.0001 for comparison between scaffold B and scaffold A.</p>
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<p>Bone cell viability and proliferation in co-cultures on the three scaffolds tested. THP-1 and SCP-1 were seeded and co-cultured on scaffolds A, BI, and BII for 21 days. Quantification of total DNA (<b>a</b>) and mitochondrial activity by resazurin conversion (<b>b</b>) in bone co-cultures after 7 days, 14 days, and 21 days. Number of live bone co-cultures were visualized by esterase activity (<b>c</b>) using calcein-AM (green) and nuclear staining with Hoechst 33342 (blue) (scale bar 2000 µm). Each measure was conducted at least three independent times in triplicate. The data are presented as the mean, standard error of the mean, and all data points. Data were analyzed by two-way analysis of variance test followed by Tukey’s multiple comparisons. <span class="html-italic">p</span>-values are classified as **** <span class="html-italic">p</span> &lt; 0.0001 for comparison between scaffold B and scaffold A and as # <span class="html-italic">p</span> &lt; 0.05 for comparison within scaffold B.</p>
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<p>Osteoblast- and osteoclast-like cell function in co-cultures on the three scaffolds tested. THP-1 and SCP-1 were seeded and co-cultured on scaffolds A, BI, and BII for 21 days. (<b>a</b>) Alkaline phosphatase (AP), (<b>b</b>) carbonic anhydrase II (CAII), and (<b>c</b>) tartrate-resistant acid phosphatase (TRAP) activity normalized to DNA of bone co-cultures were analyzed after 7 days, 14 days, and 21 days as relative absorbance units (RAU). (<b>d</b>) Procollagen type I N-propeptide (PINP) and collagen type I N-telopeptide (NTX) supernatant levels were determined after a 21-day culture. Each measure was conducted at least three independent times in duplicate. The data are presented as the mean or standard error of the mean. Data were analyzed by a two-way analysis of variance test followed by Tukey’s multiple comparisons. <span class="html-italic">p</span>-values are classified as **** <span class="html-italic">p</span> &lt; 0.0001, ** <span class="html-italic">p</span> &lt; 0.01, and * <span class="html-italic">p</span> &lt; 0.05 for comparison between scaffold B and scaffold A and as ## <span class="html-italic">p</span> &lt; 0.01 for comparison within scaffold B.</p>
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36 pages, 3578 KiB  
Review
2D and 3D Nanostructured Metal Oxide Composites as Promising Materials for Electrochemical Energy Storage Techniques: Synthesis Methods and Properties
by Cornelia Bandas, Corina Orha, Mircea Nicolaescu, Mina-Ionela Morariu (Popescu) and Carmen Lăzău
Int. J. Mol. Sci. 2024, 25(23), 12521; https://doi.org/10.3390/ijms252312521 - 21 Nov 2024
Abstract
Due to population growth and global technological development, energy consumption has increased exponentially. The global energy crisis opens up many hotly debated topics regarding energy generation and consumption. Not only is energy production in short supply due to limited energy resources but efficient [...] Read more.
Due to population growth and global technological development, energy consumption has increased exponentially. The global energy crisis opens up many hotly debated topics regarding energy generation and consumption. Not only is energy production in short supply due to limited energy resources but efficient and sustainable storage has become a very important goal. Currently, there are energy storage devices such as batteries, capacitors, and super-capacitors. Supercapacitors or electrochemical capacitors can be very advantageous replacements for batteries and capacitors because they can achieve higher power density and energy density characteristics. The evolution and progress of society demand the use of innovative and composite nanostructured metal oxide materials, which fulfill the requirements of high-performance technologies. This review mainly addresses the synthesis techniques and properties of 2D and 3D metal oxide nanostructured materials, especially based on Ti, Fe, Ga, and Sn ions, electrochemical methods used for the characterization and application of 2D, and 3D nanostructured metal oxide structures in electrochemical storage systems of energy. Full article
20 pages, 3708 KiB  
Article
Effect of Natural Fiber and Biomass on Acoustic Performance of 3D Hybrid Fabric-Reinforced Composite Panels
by Shabnam Nazari, Tatiana Alexiou Ivanova, Rajesh Kumar Mishra, Miroslav Müller, Mehdi Akhbari and Zohreh Esfahani Hashjin
Materials 2024, 17(23), 5695; https://doi.org/10.3390/ma17235695 - 21 Nov 2024
Abstract
This research investigated the sound insulation performance of 3D woven hybrid fabric-reinforced composites using natural fibers, such as jute, along with E-glass and biomass derived from agro-waste, e.g., coffee husk and waste palm fiber. The composites made from pure E-glass, pure jute, and [...] Read more.
This research investigated the sound insulation performance of 3D woven hybrid fabric-reinforced composites using natural fibers, such as jute, along with E-glass and biomass derived from agro-waste, e.g., coffee husk and waste palm fiber. The composites made from pure E-glass, pure jute, and hybrid glass–jute configurations were tested for sound absorbance at frequencies of 1000 Hz and 10,000 Hz. A sound insulation chamber was used for measuring the sound reduction levels. Results show that the sound insulation performance of the panels was remarkably enhanced with composites containing natural fiber reinforcements. The jute-based composites provided the maximum insulation of sound, with waste palm fiber fillers in particular. At a frequency of 10,000 Hz, a noise reduction reaching 44.9 dB was observed. The highest sound absorption was observed in the 3D woven jute composites with the additive of waste palm fiber, which outperformed the other samples. When comparing the effect of coffee husk and palm fiber as biomass fillers, both exhibited notable improvements in sound insulation, but the palm fiber generally performed better across different samples. Although panels containing palm fiber additives appeared to reduce sound more than those containing coffee husk, statistical analysis revealed no significant difference between the two, indicating that both are efficient and eco-friendly fillers for soundproofing applications. One-way analysis of variance (ANOVA) confirmed the significance of the effect of reinforcing structures and biofillers on acoustic performance. This study demonstrated the possibility of using sustainable green materials for soundproofing applications within various industries. Full article
(This article belongs to the Section Green Materials)
13 pages, 5425 KiB  
Article
Highly Sensitive SnS2/rGO-Based Gas Sensor for Detecting Chemical Warfare Agents at Room Temperature: A Theoretical Study Based on First-Principles Calculations
by Ting Liang, Huaizhang Wang, Huaning Jiang, Yelin Qi, Rui Yan, Jiangcun Li and Yanlei Shangguan
Crystals 2024, 14(12), 1008; https://doi.org/10.3390/cryst14121008 - 21 Nov 2024
Abstract
Chemical warfare agents (CWAs) are known as poor man’s bombs because of their small lethal dose, cheapness, and ease of production. Therefore, the highly sensitive and rapid detection of CWAs at room temperature (RT = 25 °C) is essential. In this paper, we [...] Read more.
Chemical warfare agents (CWAs) are known as poor man’s bombs because of their small lethal dose, cheapness, and ease of production. Therefore, the highly sensitive and rapid detection of CWAs at room temperature (RT = 25 °C) is essential. In this paper, we have developed a resistive semiconductor sensor for the highly sensitive detection of CWAs at RT. The gas-sensing material is SnS2/rGO nanosheets (NSs) prepared by hydrothermal synthesis. The lower detection limits of the SnS2/rGO NSs-based gas sensor were 0.05 mg/m3 and 0.1 mg/m3 for the typical chemical weapons sarin (GB) and sulfur mustard (HD), respectively. The responsivity can reach −3.54% and −10.2% in 95 s for 1.0 mg/m3 GB, and in 47 s for 1.0 mg/m3 HD. They are 1.17 and 2.71 times higher than the previously reported Nb-MoS2 NSs-based gas sensors, respectively. In addition, it has better repeatability (RSD = 6.77%) and stability for up to 10 weeks (RSD = 20.99%). Furthermore, to simplify the work of later researchers based on the detection of CWAs by two-dimensional transition metal sulfur compounds (2D-TMDCs), we carried out calculations of the SnS2 NSs-based and SnS2/rGO NSs-based gas sensor-adsorbing CWAs. Detailed comparisons are made in conjunction with experimental results. For different materials, it was found that the SnS2/rGO NSs-based gas sensor performed better in all aspects of adsorbing CWAs in the experimental results. Adsorbed CWAs at a distance smaller than that of the SnS2 NSs-based gas sensor in the theoretical calculations, as well as its adsorption energy and transferred charge, were larger than those of the SnS2 NSs-based gas sensor. For different CWAs, the experimental results show that the sensitivity of the SnS2/rGO NSs-based gas sensor for the adsorption of GB is higher than that of HD, and accordingly, the theoretical calculations show that the adsorption distance of the SnS2/rGO NSs-based gas sensor for the adsorption of GB is smaller than that of HD, and the adsorption energy and the amount of transferred charge are larger than that of HD. This regularity conclusion proves the feasibility of adsorption of CWAs by gas sensors based on SnS2 NSs, as well as the feasibility and reliability of theoretical prediction experiments. This work lays a good theoretical foundation for subsequent rapid screenings of gas sensors with gas-sensitive materials for detecting CWAs. Full article
(This article belongs to the Special Issue Organic Photonics: Organic Optical Functional Materials and Devices)
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Figure 1

Figure 1
<p>(<b>a</b>) Sensor electrode physical picture; (<b>b</b>) SEM images of the SnS<sub>2</sub>/rGO NSs; (<b>c</b>) TEM images of the SnS<sub>2</sub>/rGO NSs; (<b>d</b>) the high-resolution TEM image.</p>
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<p>SnS<sub>2</sub>/rGO (<b>a</b>) XRD characterization; (<b>b</b>) Raman spectra; (<b>c</b>) EDS elemental mapping.</p>
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<p>The response–recovery curve of the SnS<sub>2</sub> and SnS<sub>2</sub>/rGO NSs-based gas sensor was exposed to various concentrations of (<b>a</b>) GB and (<b>b</b>) HD vapor ranging from 0.05 to 1.5 mg/m<sup>3</sup>. (<b>c</b>) Three successive sensing cycles of the SnS<sub>2</sub> NSs-based and SnS<sub>2</sub>/rGO NSs-based gas sensors were continuously exposed to 0.1 mg/m<sup>3</sup> GB. (<b>d</b>) Long-term stability of the SnS<sub>2</sub>/rGO NSs-based gas sensor was exposed to 0.5 mg/m<sup>3</sup> GB for ten weeks.</p>
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<p>Sensing schematic diagram of SnS<sub>2</sub>/rGO NSs (<b>a</b>) in air and (<b>b</b>) adsorption GB.</p>
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<p>Structural modeling of (<b>a</b>) SnS<sub>2</sub>; (<b>b</b>) SnS<sub>2</sub>/rGO; (<b>c</b>) GB; and (<b>d</b>) HD. Optimal adsorption sites of GB on (<b>e</b>) SnS<sub>2</sub> and (<b>f</b>) SnS<sub>2</sub>/rGO surfaces. Optimal adsorption sites of HD on (<b>g</b>) SnS<sub>2</sub> and (<b>h</b>) SnS<sub>2</sub>/rGO surfaces.</p>
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<p>Differential charge-density plots of SnS<sub>2</sub> adsorption on (<b>a</b>) GB and (<b>b</b>) HD; differential charge-density plots of SnS<sub>2</sub>/GO adsorption on (<b>c</b>) GB and (<b>d</b>) HD. (The isosurfaces take the value of 0.02 eV/Å. Green is the region of concentration of electrons. Light blue is the region of dissipation of electrons).</p>
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<p>(<b>a</b>) Energy band structure and (<b>b</b>) density-of-state plots for SnS<sub>2</sub>. (<b>c</b>) Energy band structure and (<b>d</b>) density-of-state plots for SnS<sub>2</sub>/rGO. (<b>e</b>) Energy band structure and (<b>f</b>) density-of-state plots of SnS<sub>2</sub>/rGO NSs-adsorbed GB. (<b>g</b>) Energy band structure and (<b>h</b>) density-of-state plots of SnS<sub>2</sub>/rGO NSs-adsorbed HD.</p>
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11 pages, 1191 KiB  
Article
A Prospective Study of Nephrocalcinosis in Very Preterm Infants: Incidence, Risk Factors and Vitamin D Intake in the First Month
by Rasa Garunkstiene, Ruta Levuliene, Andrius Cekuolis, Rimante Cerkauskiene, Nijole Drazdiene and Arunas Liubsys
Medicina 2024, 60(12), 1910; https://doi.org/10.3390/medicina60121910 - 21 Nov 2024
Viewed by 83
Abstract
Background and objectives: Nephrocalcinosis (NC) is a common condition characterized by the deposition of calcium salts in the kidneys of very preterm infants due to tubular immaturity, intensive treatment and nutritional supplements. However, optimal vitamin D supplementation remains unclear. In most patients, [...] Read more.
Background and objectives: Nephrocalcinosis (NC) is a common condition characterized by the deposition of calcium salts in the kidneys of very preterm infants due to tubular immaturity, intensive treatment and nutritional supplements. However, optimal vitamin D supplementation remains unclear. In most patients, NC spontaneously resolves within the first year of life, but long-term kidney function data are lacking. The aim was to study nephrocalcinosis in very preterm infants, assess risk factors and evaluate vitamin D’s impact during the first month with a 2-year follow-up. Material and Methods: This was a prospective observational study conducted over a 3-year period in infants with a gestational age of less than 32 weeks. The patients’ data were compared between the NC and control groups based on kidney ultrasound results at discharge. In the first month, the mean vitamin D intake from all sources as well as biochemical markers of calcium metabolism were collected. Patients diagnosed with NC were referred to a pediatric nephrologist after discharge. Results: NC was found in 35% of a cohort of 160 infants, more common in those with a gestational age <28 weeks. Risk factors were associated with higher morbidity and necessary treatment. At 28 days, serum 25-hydroxy vitamin D levels differed between NC and control groups (p < 0.05). The NC group with GA ≥ 28 weeks had higher vitamin D intake (p < 0.05), hypercalciuria and calcium/creatinine ratio (p < 0.01) and lower parathyroid hormone levels (p < 0.05). Follow-up showed resolution in 70% at 12 months and 90% at 24 months. Conclusions: The prevalence of NC in very preterm infants is significant, associated with lower maturity and higher morbidity. Careful vitamin D supplementation and biochemical monitoring of Ca metabolism from the first month of life should support bone health and limit the risk of nephrocalcinosis. Due to the high incidence of NC in very preterm infants, long-term follow-up is essential. Full article
(This article belongs to the Section Pediatrics)
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Figure 1
<p>Flow chart.</p>
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<p>Average vitamin D intake in µg/kg during the first 28 days (5 µg—200 IU). Serum 25(OH)D—serum 25-hydroxyvitamin D; d.—days. Different symbols for control ● and nephrocalcinosis ▲ groups. Serum 25(OH)D levels at 30 and 50 ng/mL (optimal concentration) are marked as dotted lines.</p>
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<p>Probability of nephrocalcinosis by gestational age and the mean daily intake of vitamin D. Gestational groups (&lt;28 weeks and ≥28 weeks of gestational age) are presented with different line types.</p>
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<p>A decreasing trend in the probability of nephrocalcinosis for gestational age is observed when parathyroid hormone (at 28 days of life) increases. iPTH—intact parathyroid hormone. Gestational groups (&lt;28 weeks and ≥28 weeks of gestational age) are presented with different line types.</p>
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22 pages, 4119 KiB  
Article
Fast Detection of Idler Supports Using Density Histograms in Belt Conveyor Inspection with a Mobile Robot
by Janusz Jakubiak and Jakub Delicat
Appl. Sci. 2024, 14(23), 10774; https://doi.org/10.3390/app142310774 - 21 Nov 2024
Viewed by 140
Abstract
The automatic inspection of belt conveyors gathers increasing attention in the mining industry. The utilization of mobile robots to perform the inspection allows increasing the frequency and precision of inspection data collection. One of the issues that needs to be solved is the [...] Read more.
The automatic inspection of belt conveyors gathers increasing attention in the mining industry. The utilization of mobile robots to perform the inspection allows increasing the frequency and precision of inspection data collection. One of the issues that needs to be solved is the location of inspected objects, such as, for example, conveyor idlers in the vicinity of the robot. This paper presents a novel approach to analyze the 3D LIDAR data to detect idler frames in real time with high accuracy. Our method processes a point cloud image to determine positions of the frames relative to the robot. The detection algorithm utilizes density histograms, Euclidean clustering, and a dimension-based classifier. The proposed data flow focuses on separate processing of single scans independently, to minimize the computational load, necessary for real-time performance. The algorithm is verified with data recorded in a raw material processing plant by comparing the results with human-labeled objects. The proposed process is capable of detecting idler frames in a single 3D scan with accuracy above 83%. The average processing time of a single scan is under 22 ms, with a maximum of 75 ms, ensuring that idler frames are detected within the scan acquisition period, allowing continuous operation without delays. These results demonstrate that the algorithm enables the fast and accurate detection and localization of idler frames in real-world scenarios. Full article
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<p>Idler supports of typical belt conveyors: (<b>a</b>) [<a href="#B4-applsci-14-10774" class="html-bibr">4</a>], (<b>b</b>) [<a href="#B5-applsci-14-10774" class="html-bibr">5</a>].</p>
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<p>Activity diagram of point cloud processing.</p>
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<p>A scheme of the experiment location with marked robot path segments A and B.</p>
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<p>Images of the experiment location. (<b>a</b>) Path A. (<b>b</b>) Path B. Green rectangles mark the idlers’ supports to be detected.</p>
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<p>Mobile platform with the sensor module at the experiment site [<a href="#B4-applsci-14-10774" class="html-bibr">4</a>].</p>
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<p>Transformation of a point cloud in preprocessing stage. (<b>a</b>) Original image from the LIDAR sensor. The red rectangle indicates the area with conveyors. (<b>b</b>) Point cloud with distant points clipped. The boxes show the location of idler supports. (<b>c</b>) The results of the RANSAC algorithm—the ground points marked in red. (<b>d</b>) Aligned point cloud with ground removal.</p>
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<p>Two-dimensional histograms for a single scan. (<b>a</b>) Projection to the horizontal plane <math display="inline"><semantics> <msub> <mi>H</mi> <mrow> <mi>X</mi> <mi>Y</mi> </mrow> </msub> </semantics></math> with manually marked support locations. (<b>b</b>) Projection to the front plane <math display="inline"><semantics> <msub> <mi>H</mi> <mrow> <mi>Y</mi> <mi>Z</mi> </mrow> </msub> </semantics></math>, marked elongated objects.</p>
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<p>The results of the density-based segmentation (the points of interest marked in blue-green). (<b>a</b>) Points from the <math display="inline"><semantics> <mrow> <mi>X</mi> <mi>Y</mi> </mrow> </semantics></math> segmentation. (<b>b</b>) Points from the <math display="inline"><semantics> <mrow> <mi>Y</mi> <mi>Z</mi> </mrow> </semantics></math> segmentation. (<b>c</b>) The set difference of points from the <math display="inline"><semantics> <mrow> <mi>X</mi> <mi>Y</mi> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mi>Y</mi> <mi>Z</mi> </mrow> </semantics></math> segmentations.</p>
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<p>Clusters representing idler frame candidates.</p>
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<p>Examples of detection.</p>
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<p>Spatial distribution of detection results in robot local coordinates and unrestricted range. (<b>a</b>) Along Path A. (<b>b</b>) Along Path B.</p>
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<p>Detection results in areas with various theoretical numbers of active LIDAR channels. (<b>a</b>) Along Path A. (<b>b</b>) Along Path B.</p>
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<p>Spatial distribution of detection results in robot local coordinates in region limited to 6 and more LIDAR planes. (<b>a</b>) Along Path A. (<b>b</b>) Along Path B.</p>
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<p>Detection of the supports in time—X coordinate of the objects. (<b>a</b>) Path A—in the first row to the left of the robot. (<b>b</b>) Path A—in the first row to the right of the robot. (<b>c</b>) Path B—in the first row to the left of the robot.</p>
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<p>Duration of processing stages along Path A. (<b>a</b>) For each scan along the trajectory. (<b>b</b>) Box plots of the duration of stages.</p>
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<p>Duration of processing stages along Path B. (<b>a</b>) For each scan along the trajectory. (<b>b</b>) Box plots of the duration of stages.</p>
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12 pages, 2488 KiB  
Article
A Polycarbonate-Assisted Transfer Method for van der Waals Contacts to Magnetic Two-Dimensional Materials
by Kunlin Yang, Guorui Zhao, Yibin Zhao, Jie Xiao, Le Wang, Jiaqi Liu, Wenqing Song, Qing Lan, Tuoyu Zhao, Hai Huang, Jia-Wei Mei and Wu Shi
Micromachines 2024, 15(11), 1401; https://doi.org/10.3390/mi15111401 - 20 Nov 2024
Viewed by 175
Abstract
Magnetic two-dimensional (2D) materials have garnered significant attention for their potential to revolutionize 2D spintronics due to their unique magnetic properties. However, their air-sensitivity and highly insulating nature of the magnetic semiconductors present substantial challenges for device fabrication with effective contacts. In this [...] Read more.
Magnetic two-dimensional (2D) materials have garnered significant attention for their potential to revolutionize 2D spintronics due to their unique magnetic properties. However, their air-sensitivity and highly insulating nature of the magnetic semiconductors present substantial challenges for device fabrication with effective contacts. In this study, we introduce a polycarbonate (PC)-assisted transfer method that effectively forms van der Waals (vdW) contacts with 2D materials, streamlining the fabrication process without the need for additional lithography. This method is particularly advantageous for air-sensitive magnetic materials, as demonstrated in Fe3GeTe2. It also ensures excellent interface contact quality and preserves the intrinsic magnetic properties in magnetic semiconductors like CrSBr. Remarkably, this method achieves a contact resistance four orders of magnitude lower than that achieved with traditional thermally evaporated electrodes in thin-layer CrSBr devices and enables the observation of sharp magnetic transitions similar to those observed with graphene vdW contacts. Compatible with standard dry-transfer processes and scalable to large wafer sizes, our approach provides a straightforward and effective solution for developing complex magnetic heterojunction devices and expanding the applications of magnetic 2D materials. Full article
(This article belongs to the Special Issue 2D-Materials Based Fabrication and Devices)
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<p>Schematic diagram of the PC-assisted transfer method for vdW contacts. Blue arrows indicate the sequence of operations, and red dashed lines highlight the magnified areas. (<b>a</b>) Au electrode arrays fabricated on a silicon wafer using thermal evaporation after lithography. (<b>b</b>) A silicon wafer spin-coated with a PC film, where the black rectangular frame indicates the area cut with a blade, representing the portion to be used. The right panel shows an optical image under a microscope, with a scale bar of 200 μm. (<b>c</b>) Illustration of the process where the PC film with electrodes is flipped and placed onto a PDMS stamp. Left panel: schematic of the operation. The middle optical image shows the Au electrodes transferred onto the PC film during the process, with a scale bar of 200 μm. Right panel: an image of the electrodes/PC on the PDMS stamp, with bubbles near the large electrode pads that will be removed during the heated transfer. Scale bar: 200 μm. (<b>d</b>) Alignment process. The target flake of 2D materials on a substrate is precisely aligned with the electrodes on the PDMS stamp and carefully stacked together using an XYZR transfer stage. Right panel shows a photograph of the motorized transfer stage inside a glovebox. (<b>e</b>) The transferred electrodes establish van der Waals contact with the sample. The PC film is melted when heating the sample to 180 °C and then dissolved in chloroform to complete the transfer.</p>
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<p>Transfer process in a glove box and optical images on different 2D materials. (<b>a</b>) (<b>i</b>–<b>iiii</b>) Sequential images showing the entire PC-assisted transfer process for establishing vdW contacts to air-sensitive ferromagnet Fe<sub>3</sub>GeTe<sub>2</sub> inside the glovebox: (<b>i</b>) Optical image of the Au electrodes on a sacrificial silicon wafer layer, covered with spin-coated PC film. (<b>ii</b>) Cleaved few-layer Fe<sub>3</sub>GeTe<sub>2</sub> sample on a SiO<sub>2</sub>/Si substrate. (<b>iii</b>) Optical image after the transfer process, showing the electrodes and the Fe<sub>3</sub>GeTe<sub>2</sub> sample in van der Waals contact, with the melted PC film on top. (<b>iiii</b>) Optical image of the Fe<sub>3</sub>GeTe<sub>2</sub> sample with transferred Au electrodes after removing the PC film in chloroform. (<b>b</b>–<b>e</b>) Optical images of devices with transferred Au electrodes for various 2D materials, including conventional 2D material graphene (<b>b</b>) and transition metal dichalcogenide WSe<sub>2</sub> (<b>c</b>) as well as antiferromagnetic 2D materials CoPS<sub>3</sub> (<b>d</b>) and NiPS<sub>3</sub> (<b>e</b>). All scale bars are indicated in the images.</p>
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<p>Electrical transport characterization of air-sensitive ferromagnet Fe<sub>3</sub>GeTe<sub>2</sub> device with the PC-assisted transferred Au electrodes. (<b>a</b>) Four-terminal resistance Rxx versus temperature curve of the Fe<sub>3</sub>GeTe<sub>2</sub> device, showing metallic behavior with good contact properties. The optical image of the device is shown in <a href="#micromachines-15-01401-f002" class="html-fig">Figure 2</a>e. (<b>b</b>) Hall resistance Rxy as a function of magnetic field measured at various temperatures from 2 K to 180 K (indicated on the right), showing clear anomalous Hall effect in the Fe<sub>3</sub>GeTe<sub>2</sub> device. As the temperature increases, the coercive field gradually decreases, and the hysteresis is minimal at 160 K. This trend reflects the material’s robust ferromagnetic properties at lower temperatures.</p>
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<p>Comparison of contacts in CrSBr-based antiferromagnetic semiconductor devices. (<b>a</b>,<b>b</b>) Optical images of CrSBr devices with thermally evaporated Au electrodes (<b>a</b>) and PC-assisted transferred Au electrodes (<b>b</b>), with the crystal axes “a” and “b” marked in each image. All electrodes are numbered for easy identification of measurement configurations. (<b>c</b>,<b>d</b>) I–V curves measured using the central electrodes for the devices displayed above, from which the two-terminal contact resistance (<span class="html-italic">R</span><sub>2T</sub>) is determined based on the slope. (<b>e</b>,<b>f</b>) Four-terminal channel resistance (<span class="html-italic">R</span><sub>4T</sub>) for each device, calculated as <span class="html-italic">R</span><sub>4T</sub> = V/I. Here, a voltage (V<sub>DS</sub>) is applied across the outermost electrodes to measure the channel current (I), while voltage (V) is monitored at the central electrodes, which are labeled in the figure inserts.</p>
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<p>Transport properties of the antiferromagnetic semiconductor CrSBr measured with different types of contacts. (<b>a</b>) Normalized conductance (defined as G/G (T = 300 K)) as a function of temperature (T) measured for CrSBr devices with various thicknesses and types of contacts. (<b>b</b>) Comparison of normalized conductance-vs.-temperature curve for the initial cooling-down process with the curve for the warming-up process after prolonged low-temperature measurements for a few-layer CrSBr device with PC-assisted transferred electrodes. (<b>c</b>) Magnetoresistance ratio, defined as MR (%) = (<span class="html-italic">R</span>(B) − <span class="html-italic">R</span>(0T))/<span class="html-italic">R</span>(0T) measured at various temperatures for the same few-layer CrSBr devices in (<b>b</b>). The external magnetic field applied along the c-axis (perpendicular to the a,b-plane). (<b>d</b>) Magnetoresistance ratio measured at 10 K for the bilayer CrSBr devices with PC-assisted transferred Au electrodes, graphene electrodes, and thermally evaporated Au electrodes. The external magnetic field applied along the easy axis (b-axis of CrSBr).</p>
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11 pages, 3468 KiB  
Article
Large-Scale Atomistic Simulation of Sintering Process and Mechanical Properties of Al Matrix Composite with Different Reinforcements
by Yongchao Zhu, Can Sui, Na Li, Lijuan Sun and Songtao Li
Metals 2024, 14(11), 1312; https://doi.org/10.3390/met14111312 - 20 Nov 2024
Viewed by 201
Abstract
Through molecular dynamics methods, composite models built with a large scale were employed to investigate the effects of different reinforcements, which were different from those used in most of the similar studies, where only a graphene nanosheet (GNS) or a rigid spherical particle [...] Read more.
Through molecular dynamics methods, composite models built with a large scale were employed to investigate the effects of different reinforcements, which were different from those used in most of the similar studies, where only a graphene nanosheet (GNS) or a rigid spherical particle was embedded in a metal matrix. Here, 27 GNSs or diamond particles were placed in the empty spaces between Al particles with random directions. Then, Al matrix composites were prepared by modeling a sintering process. Structural analysis and tensile modeling were carried out on the sintered composites. The results indicate that the density of the Al–graphene composite was higher and increased with growth in the size of the reinforcements, although the Al–graphene system required more heating time to achieve densification. Bigger GNSs were likely to increase the pore volume of the composite. Meanwhile, larger GNSs were also more beneficial for grain refinement, leading to growth in the ratio of Al atoms at grain boundaries. The greater impact of GNSs on the inner structure was not just derived from their high specific surface area, and this impact was enlarged if drawn as a function of the weight fraction rather than the surface area. However, tensile processes revealed that two-dimensional (2D) materials seemed to have no clear impact on the direct strengthening effect, and anisotropy could not be observed in the large-scale models. The biggest GNSs even led to reductions in both the tensile strength and ductility of the Al–graphene composite, which coincided with some experimental reports. The evolution of the inner structures indicated that GNSs have the same role as diamond particles in dislocation accumulation and crack propagation. The major advantage of GNSs is their ability to improve the densification and grain refinement of the metal matrix composite (MMC). Full article
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<p>Models of composite systems before sintering. (<b>a</b>) Al–graphene system. (<b>b</b>) Al–diamond system.</p>
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<p>The volumes of the composites as a function of the sintering time.</p>
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<p>The densities of the composites as functions of the surface area (<b>a</b>) and weight fraction (<b>b</b>).</p>
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<p>Inner structures of composites, where Al atoms are colored based on CSP values and reinforcements are tinted black.</p>
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<p>The ratios of Al atoms at grain boundaries and the pore volumes of the composites as functions of the surface area (<b>a</b>) and weight fraction (<b>b</b>).</p>
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<p>The tensile strength and elongation values of the composites as functions of the surface area (<b>a</b>) and weight fraction (<b>b</b>).</p>
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<p>The stress–strain curves of the composites stretched in the Y direction (<b>a</b>) and the evolution of the inner structures at different strains (<b>b</b>).</p>
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11 pages, 4525 KiB  
Article
Influence of Simulated Skin Color on the Accuracy of Face Scans
by Ido Brintouch, Aisha Ali, Georgios E. Romanos and Rafael A. Delgado-Ruiz
Prosthesis 2024, 6(6), 1372-1382; https://doi.org/10.3390/prosthesis6060099 - 20 Nov 2024
Viewed by 213
Abstract
Aims: this study aims to investigate the impact of simulated skin color and the use of fiducial markers on the accuracy of 3D facial scans, comparing two types of structured light scanners under constant ambient lighting conditions. Materials and Methods: Three mannequins with [...] Read more.
Aims: this study aims to investigate the impact of simulated skin color and the use of fiducial markers on the accuracy of 3D facial scans, comparing two types of structured light scanners under constant ambient lighting conditions. Materials and Methods: Three mannequins with different skin colors—black, white, and pink—were scanned using two light based hand-held scanners (infrared light and blue-light). Each mannequin was scanned with and without fiducial markers placed on defined anatomical landmarks. A total of one hundred thirty-two scans were performed and converted into standard tessellation language (STL) files. STL files from each scanner were compared to their respective control scans using point cloud comparison software. Accuracy was evaluated based on root mean square (RMS) values. Descriptive statistics summarized the data, and a t-test was performed to assess differences in RMS values between scans with and without fiducial markers for each scanner type. Results: The infrared light scanner showed the highest accuracy for the white mannequin, as evidenced by lower RMS values compared to the pink and black mannequins. Adding fiducial markers significantly enhanced scan accuracy for the pink and black mannequins. The blue-light scanner achieved accuracy for the white and pink mannequins comparable to that of the infrared scanner. However, it was unable to scan the black mannequin, even with the use of markers. Conclusions: Within the limitations of this study, simulated skin color significantly affects the accuracy of facial 3D scans. Scans of lighter (white) tones demonstrate higher accuracy compared to darker tones. Fiducial markers enhance the accuracy for an infrared scanner; however, a blue-light scanner is unable to capture dark simulated skin, even with the addition of fiducial markers. Full article
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<p>Frontal and a lateral view of the mannequin heads with fiducial markers placed. Nine locations were marked: left and right exocanthion, left and right cheilion, the pogonion, the philtrum, the right and left helical crus of the ears, and the glabella.</p>
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<p>A red arrow pointing to the rotating base/platform placed below each mannequin.</p>
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<p>Scanners used in this experiment. The image shows the infrared light scanner (<b>a</b>) and the blue light scanner (<b>b</b>) mounted on a tripod.</p>
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<p>Setting scanning distance. The image shows one of the mannequin heads on the rotational base, a meter with the set distance, and the camera mounted in the tripod.</p>
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<p>Illustrative images of white mannequin heads showing scans overlaid on the control scan. The left image includes fiducial markers, while the right image does not. The color scale represents the RMS values, indicating the accuracy of the scans. Best accuracy of all groups achieved with the white mannequins.</p>
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<p>Illustrative images of pink mannequin heads with scans overlaid on the control scan. The left image includes fiducial markers, while the right image does not. The color scale represents the RMS values, indicating scan accuracy. Accuracy on pink mannequins was lower than on white mannequins but higher than on black mannequins.</p>
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<p>Illustrative images of black mannequin heads with scans overlaid on the control scan. The left image includes fiducial markers, while the right image does not. The color scale represents the RMS values, indicating scan accuracy. Accuracy on black mannequins was the lowest of all groups (white and pink).</p>
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<p>Infrared scanner. Box-plot comparison of RMS values for object color scans in white (W), pink (P), and black (B) mannequins with (T) and without markers (C). The asterisk (*) represents outlier.</p>
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<p>Blue-light Scanner. Box-plot comparison of RMS values for object color scans in white (W), pink (P), and black (B) mannequins with (T) and without markers (C). The asterisk (*) represents outlier.</p>
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11 pages, 2838 KiB  
Article
The Synthesis of a Large Stokes-Shift Dye and Intercalation into the Nanochannels of Zeolite L
by Fabian Walther, Achim Ecker, Dominik Brühwiler and Marc Bornand
Materials 2024, 17(22), 5669; https://doi.org/10.3390/ma17225669 - 20 Nov 2024
Viewed by 242
Abstract
A host–guest-based fluorescent composite with a large Stokes shift was synthesized by intercalating 2,2′-(thiophene-2,5-diyl)bis(benzo[d]oxazol-6-amine) (BBTA) into the nanochannels of zeolite L (ZL) and sealing the pores with (3-aminopropyl)triethoxysilane (APTES). To confirm the orientation of the amino groups in BBTA, a single crystal of [...] Read more.
A host–guest-based fluorescent composite with a large Stokes shift was synthesized by intercalating 2,2′-(thiophene-2,5-diyl)bis(benzo[d]oxazol-6-amine) (BBTA) into the nanochannels of zeolite L (ZL) and sealing the pores with (3-aminopropyl)triethoxysilane (APTES). To confirm the orientation of the amino groups in BBTA, a single crystal of 2,5-bis(6-nitrobenzo[d]oxazol-2-yl)thiophene (BBTN) was grown and examined by X-ray crystallography. The evidence of successful intercalation of BBTA into the nanochannels of ZL was provided by fluorescence spectrometry, gas sorption and fluorescence microscopy. BBTA showed a Stokes shift of 6641 cm−1 (157 nm) in ethanol and 4611 cm−1 (93 nm) in toluene. The BBTA-ZL composite (BBTA-ZL-s) showed a Stokes shift of 5677 cm−1 (123 nm) in toluene, and 5450 cm−1 (124 nm) in ethanol. In addition, the degree of loading was determined and stability against leaching was confirmed. We report the synthesis of this novel composite dye material with potential applications where free dyes are not applicable and which retains a large Stokes shift, independent of its chemical environment. Full article
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<p>Reaction scheme for the production of BBTA starting from BBT via BBTN. BBT is first nitrated with a nitrating acid and then the nitro groups are reduced.</p>
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<p>X-ray structure of BBTN (<b>left</b>) and the corresponding unit cell (<b>right</b>). Created with VESTA ver. 3.5.8 based on the cif-file deposited at CCDC with number 2252524.</p>
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<p>Stokes shift in BBTA (66 µg·mL<sup>−1</sup>) in (<b>a</b>) wavelength and (<b>b</b>) wavenumber in different solvents. The maxima, blue for excitation and red for emission, are highlighted. The Stokes shift is shown as a gray bar. The exact excitation and emission wavelength maxima are listed in <a href="#app1-materials-17-05669" class="html-app">Tables S1 and S2</a>.</p>
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<p>Normalized (I<sub>norm</sub>) excitation spectrum (blue) and the emission spectrum (orange) of BBTA (66 µg·mL<sup>−1</sup>) in ethanol.</p>
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<p>Three-dimensional fluorescence spectra measured in toluene (<b>left column</b>) and in ethanol (<b>right column</b>). From top to bottom: BBTA in solution (66 µg·mL<sup>−1</sup>), BBTA on the external surface of ZL (Impregnated, 333 µg·mL<sup>−1</sup>), BBTA-ZL (333 µg·mL<sup>−1</sup>), and BBTA-ZL-s (333 µg·mL<sup>−1</sup>). The excitation wavelength is plotted on the <span class="html-italic">y</span>-axis and the emission wavelength is plotted on the <span class="html-italic">x</span>-axis.</p>
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<p>Nitrogen sorption isotherms at 77 K of pristine ZL (blue) and BBTA-ZL (red). The adsorption isotherms are shown as solid circles and the desorption isotherms as hollow circles. Adsorption and desorption branches coincide.</p>
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<p>Fluorescence microscopy images of BBTA-ZL. The images show two crystals with a length of ca. 6.5 µm. For both crystals, the c-axis corresponds to the longer axis of the crystals. Image (<b>a</b>) was taken without a polarizer. The double arrows in images (<b>b</b>,<b>c</b>) indicate the direction of the polarizer.</p>
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<p>Stokes shift in BBTA (66 µg·mL<sup>−1</sup>) and BBTA-ZL-s (333 µg·mL<sup>−1</sup>) in (<b>a</b>) wavelength and (<b>b</b>) wavenumber in toluene and ethanol. The maxima, blue for excitation and red for emission, are highlighted. The Stokes shift is shown as a gray bar. The exact excitation and emission wavelength maxima are listed in <a href="#app1-materials-17-05669" class="html-app">Tables S3 and S4</a>.</p>
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36 pages, 9567 KiB  
Review
Two-Dimensional MoS2-Based Photodetectors
by Leilei Ye, Xiaorong Gan and Romana Schirhagl
Sustainability 2024, 16(22), 10137; https://doi.org/10.3390/su162210137 - 20 Nov 2024
Viewed by 173
Abstract
Nanomaterials can significantly improve the analytical performance of optical sensors for environmental pollutants. Two-dimensional (2D) molybdenum sulfide (MoS2) exhibits some unique physicochemical properties, such as strong light–matter interactions, bandgap tunability, and high carrier mobility, which are beneficial for constructing flexible optoelectronic [...] Read more.
Nanomaterials can significantly improve the analytical performance of optical sensors for environmental pollutants. Two-dimensional (2D) molybdenum sulfide (MoS2) exhibits some unique physicochemical properties, such as strong light–matter interactions, bandgap tunability, and high carrier mobility, which are beneficial for constructing flexible optoelectronic devices. In this review, the principle and classification of 2D MoS2-based photodetectors (PDs) are introduced, followed by a discussion about the physicochemical properties of 2D MoS2, as well as the structure–property relationships of 2D MoS2-based photoactive materials for PDs to understand the modulation strategies for enhancing the photodetection performance. Furthermore, we discuss significant advances in the surface modification and functionalization of 2D MoS2 for developing high-performance PDs, particularly focusing on synthesis pathways, modification strategies, and underlying physiochemical mechanisms for enhanced photodetection capabilities. Finally, conclusions and research perspectives on resolving significant bottlenecks or remaining challenges are offered based on recent developments in 2D MoS2-based PDs. Full article
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<p>Challenges of using pristine 2D MoS<sub>2</sub> in PDs and typical strategies for improving photodetection performances.</p>
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<p>Metal plasmonic structure dynamics. (<b>a</b>) Electron behavior in a plasmonic NP under solar illumination. (<b>b</b>) A mechanical harmonic oscillator is used to explain the coherent electronic cloud on the metal surface under light forces. Reproduced with permission from ref. [<a href="#B74-sustainability-16-10137" class="html-bibr">74</a>]. Copyright 2019, American Chemical Society.</p>
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<p>Schematic of three typical optical resonance cavities. (<b>a</b>) Fabry–Perot-type cavity. (<b>b</b>) The 2D photonic crystal cavity. (<b>c</b>) Whispering gallery mode microcavity. Reproduced with permission from ref. [<a href="#B92-sustainability-16-10137" class="html-bibr">92</a>]. Copyright 2020 John Wiley &amp; Sons, Inc.</p>
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<p>(<b>a</b>) Photoresponse of defective-MoS<sub>2</sub> PDs under vacuum or when exposed to air. (<b>b</b>) Gas response of a defective MoS<sub>2</sub> PD with and without MA<sub>3</sub>Bi<sub>2</sub>Br<sub>9</sub> treatment. (<b>c</b>) The schematic illustration of defect states in the electronic band of MoS<sub>2</sub>. Reproduced with permission from ref. [<a href="#B103-sustainability-16-10137" class="html-bibr">103</a>]. Copyright 2018 American Chemical Society.</p>
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<p>Band structures of bulk MoS<sub>2</sub> (<b>a</b>), quadrilayer MoS<sub>2</sub> (<b>b</b>), bilayer MoS<sub>2</sub> (<b>c</b>), and monolayer MoS<sub>2</sub> (<b>d</b>). Reproduced with permission from ref. [<a href="#B116-sustainability-16-10137" class="html-bibr">116</a>]. Copyright 2010 American Chemical Society.</p>
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<p>(<b>a</b>) Schematic presentation of the synthesis processes of wrinkly MoS<sub>2</sub> flakes. (<b>b</b>) Optical microscopy image and (<b>c</b>) atomic force microscopy image of a wrinkled MoS<sub>2</sub> flake (<b>d</b>) Photoluminescence spectra of wrinkly MoS<sub>2</sub> flakes at different locations (flat and wrinkly parts). (<b>e</b>) Relationship between the direct bandgap transition and the localized tensile strain. Reproduced with permission from ref. [<a href="#B114-sustainability-16-10137" class="html-bibr">114</a>]. Copyright 2013 American Chemical Society.</p>
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<p>(<b>a</b>) The relationship between the S/Mo ratio (<span class="html-italic">x</span>) and bandgaps of 2D MoS<span class="html-italic"><sub>x</sub></span>. (<b>b</b>) Interface energy band diagram between Au electrodes and 2D MoS<span class="html-italic"><sub>x</sub></span> before (<b>b</b>) and after (<b>c</b>) applying THz radiation. Electron-transport behavior in PDs based on 2D MoS<span class="html-italic"><sub>x</sub></span> with (<b>d</b>) and without (<b>e</b>) applying THz radiation. (<b>f</b>) The relationship between the photocurrent or <b>R</b> and bias voltage. Reproduced with permission from ref. [<a href="#B141-sustainability-16-10137" class="html-bibr">141</a>]. Copyright 2020 American Chemical Society.</p>
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<p>(<b>a</b>) A diagram showing the setup utilized in an MoS<sub>2</sub> PD. (<b>b</b>) The relationship between strain and temperature of polycarbonate. (<b>c</b>) Differential reflectance spectra measured at different temperatures. Reproduced with permission from ref. [<a href="#B149-sustainability-16-10137" class="html-bibr">149</a>]. Copyright 2019 Elsevier.</p>
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<p>Graphical illustration of mixed-dimensional heterostructures with different combination formats including (<b>a</b>) 0D/2D, (<b>b</b>) 1D/2D, and (<b>c</b>) 2D/3D mix-dimensional structures.</p>
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<p>(<b>a</b>) Schematic presentation of LSPR in Au-NP grating. (<b>b</b>) Extinction spectra of different Au NPs and (<b>c</b>) transfer characteristics of the Au-NP/MoS<sub>2</sub> PD. Reproduced with permission from ref. [<a href="#B170-sustainability-16-10137" class="html-bibr">170</a>]. Copyright 2020 American Chemical Society. (<b>d</b>) Schematic diagrams of Au-MoS<sub>2</sub>-Au PDs. (<b>e</b>) Light intensity-dependent <b>R</b> of Au-MoS<sub>2</sub> and Au-MoS<sub>2</sub>-Au PDs. (<b>f</b>) Schematic presentation of the interface energy band of Au-MoS<sub>2</sub>-Au. (<b>g</b>) Calculated electrical field strength distributions of Au NPs on the two surfaces of MoS<sub>2</sub>. (<b>h</b>) Photocurrents of Au-MoS<sub>2</sub>-Au PDs under different light intensities. (<b>i</b>) Possible charge-transfer processes of Au-MoS<sub>2</sub>-Au PDs under visible light. Reproduced with permission from ref. [<a href="#B171-sustainability-16-10137" class="html-bibr">171</a>]. Copyright 2022 American Chemical Society.</p>
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<p>(<b>a</b>) Schematic representation of MoS<sub>2</sub> PD (MNPs refer to the MXene QDs with an average size of 8 nm). (<b>b</b>) I-V plots of pristine MoS<sub>2</sub> and MXene-QD/MoS<sub>2</sub> PD in the dark. Two-dimensional photoresponse maps of (<b>c</b>) MXene-QD/MoS<sub>2</sub> PDs and (<b>d</b>) pristine MoS<sub>2</sub> under 635 nm excitation wavelengths. Reproduced with permission from ref. [<a href="#B176-sustainability-16-10137" class="html-bibr">176</a>]. Copyright 2022 American Chemical Society.</p>
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<p>(<b>a</b>) A 3D schematic representation of SnS<sub>2</sub>-QDs/MoS<sub>2</sub> PD. (<b>b</b>) Schematic illustration of band structures of SnS<sub>2</sub> QDs and monolayer MoS<sub>2</sub>. (<b>c</b>) <b>R</b> of SnS<sub>2</sub>-QDs/MoS<sub>2</sub> PD. Reproduced with permission from ref. [<a href="#B174-sustainability-16-10137" class="html-bibr">174</a>]. Copyright 2022 American Chemical Society.</p>
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<p>Device structure and interfacial charge-carrier transport behavior for n-ZnO/p-MoS<sub>2</sub> PDs with a forward biasing voltage (<b>a</b>), with a forward biasing voltage and under UV light (<b>b</b>), and with a forward biasing voltage and under green light (<b>c</b>). Reproduced with permission from ref. [<a href="#B182-sustainability-16-10137" class="html-bibr">182</a>]. Copyright 2020 John Wiley &amp; Sons, Inc.</p>
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<p>Schematic presentation of the device structure (<b>a</b>), the plot of <b>R</b> vs. wavelength (<b>b</b>), and the plot of current vs. decay time (<b>c</b>) for the 2D-MoS<sub>2</sub>/1D-CuO heterojunction PD. Reproduced with permission from ref. [<a href="#B184-sustainability-16-10137" class="html-bibr">184</a>]. Copyright 2016 American Chemical Society. (<b>d</b>) Schematic diagram of the PD device based on vertical MoS<sub>2</sub> nanosheets/p-GaN NRs. (<b>e</b>) SEM image of vertical MoS<sub>2</sub> nanosheets. (<b>f</b>) The dark and illuminated I-V curves of the PD device. Reproduced with permission from ref. [<a href="#B187-sustainability-16-10137" class="html-bibr">187</a>]. Copyright 2019 American Chemical Society.</p>
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<p>(<b>a</b>) Schematic presentation of the device structure of an MoS<sub>2</sub>/CsPbBr<sub>3</sub> PD. Charge production and transport processes at the MoS<sub>2</sub>/CsPbBr<sub>3</sub> heterojunction in the dark (<b>b</b>) and under light illumination (<b>c</b>). (<b>d</b>) UV-vis absorption spectra of the MoS<sub>2</sub>, CsPbBr<sub>3</sub>, and MoS<sub>2</sub>/CsPbBr<sub>3</sub> heterojunction. (<b>e</b>) I–V characteristics plots of the MoS<sub>2</sub>, CsPbBr<sub>3</sub>, and MoS<sub>2</sub>/CsPbBr<sub>3</sub> heterojunction with and without laser illumination. (<b>f</b>) Relationship between <b>R</b> and power intensity. Reproduced with permission from ref. [<a href="#B191-sustainability-16-10137" class="html-bibr">191</a>]. Copyright 2018 American Chemical Society.</p>
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<p>(<b>a</b>) Schematic presentation of the device structure of graphene/2D MoS<sub>2</sub> PD under illumination. (<b>b</b>) A diagram of the photocurrent generation of graphene/2D MoS<sub>2</sub> PD. (<b>c</b>) Current–voltage curve of graphene/2D MoS<sub>2</sub> PD in the dark and under 100 mW/cm<sup>2</sup> illumination. (<b>d</b>) <b>R</b> of graphene/2D MoS<sub>2</sub> PD at different wavelengths. (<b>e</b>) Photoconductivity of graphene. Reproduced with permission from ref. [<a href="#B194-sustainability-16-10137" class="html-bibr">194</a>]. Copyright 2015 American Chemical Society.</p>
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<p>(<b>a</b>) Schematic picture of a CZTS/MoS<sub>2</sub> PD. (<b>b</b>) Charge transfer mechanism at CZTS/MoS<sub>2</sub> heterojunctions. (<b>c</b>) Estimated <b>R</b> of the CZTS/MoS<sub>2</sub> heterojunction PD for various wavelengths at a bias of 6 V. Reproduced with permission from ref. [<a href="#B215-sustainability-16-10137" class="html-bibr">215</a>]. Copyright 2020 Elsevier.</p>
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<p>(<b>a</b>) Schematic presentation of 3D structures of MoS<sub>2</sub>/MoSe<sub>2</sub>/GaN heterostructures. (<b>b</b>) Schematics of the energy band diagram for the heterostructures. (<b>c</b>) Photoswitching of D<sub>1</sub>, D<sub>2</sub>, D<sub>3</sub>, and D<sub>4</sub> devices (D<sub>1</sub>, GaN/MoSe<sub>2</sub>; D<sub>2</sub>, GaN/MoS<sub>2</sub>; D<sub>3</sub>, GaN/MoS<sub>2</sub>/MoSe<sub>2</sub>; D<sub>4</sub>, GaN/MoSe<sub>2</sub>/MoS<sub>2</sub>). (<b>d</b>) UV (λ = 365 nm) intensity-dependent <b>R</b> for different device configurations. (<b>e</b>) Specific detectivity for different device configurations. Reproduced with permission from ref. [<a href="#B220-sustainability-16-10137" class="html-bibr">220</a>]. Copyright 2023 American Chemical Society.</p>
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17 pages, 26942 KiB  
Article
A Small Robot to Repair Asphalt Road Potholes
by Salvatore Bruno, Giuseppe Cantisani, Antonio D’Andrea, Giulia Del Serrone, Paola Di Mascio, Kristian Knudsen, Giuseppe Loprencipe, Laura Moretti, Carlo Polidori, Søren Thorenfeldt Ingwersen, Loretta Venturini and Marco Zani
Infrastructures 2024, 9(11), 210; https://doi.org/10.3390/infrastructures9110210 - 20 Nov 2024
Viewed by 204
Abstract
As part of the Horizon 2020 InfraROB project aimed at enhancing road safety through innovative robotic solutions, a compact autonomous vehicle has been developed to repair asphalt potholes. Central to this system is a 3D printer capable of extruding a novel cold-asphalt mixture, [...] Read more.
As part of the Horizon 2020 InfraROB project aimed at enhancing road safety through innovative robotic solutions, a compact autonomous vehicle has been developed to repair asphalt potholes. Central to this system is a 3D printer capable of extruding a novel cold-asphalt mixture, specifically designed for patching road surfaces. The printer is mounted on a small robot that autonomously navigates to potholes, while the human operator controls the operation from a secure location outside the traffic area. The system’s development involved several key steps: designing the repair mixture, constructing the 3D printer for mixture extrusion, implementing a photogrammetric technique to accurately measure pothole geometry for printing, and integrating the extrusion system with the robotic platform. Two preliminary tests were conducted in controlled environments at Sapienza University of Rome to check the reliability of calculation of the amount of material needed to fill in the potholes. Finally, the entire procedure was tested on an Italian motorway, demonstrating the system’s functionality without encountering operational issues. Full article
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<p>The robot’s dimensions [<a href="#B17-infrastructures-09-00210" class="html-bibr">17</a>].</p>
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<p>The 3D printer [<a href="#B17-infrastructures-09-00210" class="html-bibr">17</a>].</p>
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<p>The 3D printer connected to the robot.</p>
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<p>RPI 4B [<a href="#B21-infrastructures-09-00210" class="html-bibr">21</a>].</p>
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<p>The hardware platform installed on the robot.</p>
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<p>TMR path setting [<a href="#B30-infrastructures-09-00210" class="html-bibr">30</a>].</p>
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<p>The procedure flowchart.</p>
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<p>The structural connection of the printer with the robot.</p>
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<p>Scheme of the field operations.</p>
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<p>Flowchart of operations of the repair system.</p>
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<p>Test at the polyclinic site: manual monitoring of pothole.</p>
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<p>Test at the polyclinic site: pothole repair.</p>
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<p>Test at the parking lot of FCIE: plan for the potholes.</p>
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<p>Test at the parking lot of FCIE: (<b>a</b>) reconstruction of the potholes and comparison of the material weights for each pothole; (<b>b</b>) potholes lined with a thin layer of plastic; (<b>c</b>) the potholes after 120 days.</p>
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<p>Test site at A24 motorway (Italy).</p>
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<p>Pothole recording.</p>
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<p>Pothole reconstruction and volume calculation.</p>
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<p>Pothole filling in a pothole.</p>
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<p>Mixture compaction.</p>
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30 pages, 6585 KiB  
Review
Recent Progress on Advanced Flexible Lithium Battery Materials and Fabrication Process
by Mi Zhou, Daohong Han, Xiangming Cui, Jingzhao Wang, Xin Chen, Jianan Wang, Shiyi Sun and Wei Yan
Nanomaterials 2024, 14(22), 1856; https://doi.org/10.3390/nano14221856 - 20 Nov 2024
Viewed by 291
Abstract
Flexible energy storage devices have attracted wide attention as a key technology restricting the vigorous development of wearable electronic products. However, the practical application of flexible batteries faces great challenges, including the lack of good mechanical toughness of battery component materials and excellent [...] Read more.
Flexible energy storage devices have attracted wide attention as a key technology restricting the vigorous development of wearable electronic products. However, the practical application of flexible batteries faces great challenges, including the lack of good mechanical toughness of battery component materials and excellent adhesion between components, resulting in battery performance degradation or failure when subjected to different types of deformation. It is imperative to develop flexible batteries that can withstand deformation under different conditions and maintain stable battery performance. This paper reviews the latest research progress of flexible lithium batteries, from the research and development of new flexible battery materials, advanced preparation processes, and typical flexible structure design. First, the types of key component materials and corresponding modification technologies for flexible batteries are emphasized, mainly including carbon-based materials with flexibility, lithium anode materials, and solid-state electrolyte materials. In addition, the application of typical flexible structural designs (buckling, spiral, and origami) in flexible batteries is clarified, such as 3D printing and electrospinning, as well as advanced fabrication techniques commonly used in flexible materials and battery components. Finally, the limitations and coping strategies in the practical application of flexible lithium batteries are discussed, which provides new ideas for future research. Full article
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<p>Materials, process, and structure design of flexible batteries. Materials: C-base Collector. Reprinted with permission from Reference [<a href="#B4-nanomaterials-14-01856" class="html-bibr">4</a>]. Li-Wicking Hosts. Reprinted with permission from Reference [<a href="#B5-nanomaterials-14-01856" class="html-bibr">5</a>]. Solid-State Electrolytes (SSE). Reprinted with permission from Reference [<a href="#B6-nanomaterials-14-01856" class="html-bibr">6</a>]. Technics: 3DP-printing. Reprinted with permission from Reference [<a href="#B7-nanomaterials-14-01856" class="html-bibr">7</a>]. Electrostatic Spinning. Reprinted with permission from Reference [<a href="#B8-nanomaterials-14-01856" class="html-bibr">8</a>]. Electrodeposition. Reprinted with permission from Reference [<a href="#B9-nanomaterials-14-01856" class="html-bibr">9</a>]. Designs: Sectional Structure. Reprinted with permission from Reference [<a href="#B10-nanomaterials-14-01856" class="html-bibr">10</a>]. Spiral Structure. Reprinted with permission from Reference [<a href="#B11-nanomaterials-14-01856" class="html-bibr">11</a>]. Scale Structure. Reprinted with permission from Reference [<a href="#B12-nanomaterials-14-01856" class="html-bibr">12</a>].</p>
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<p>CNTs and graphene based flexible electrode materials. (<b>a</b>) The synthesis procedure of the MnO<sub>x</sub>/MWCNTs nanocomposites. Reprinted with permission from Reference [<a href="#B24-nanomaterials-14-01856" class="html-bibr">24</a>]. (<b>b</b>) The preparation procedure of flexible C@Fe<sub>2</sub>O<sub>3</sub>/SWCNT membrane. Reprinted with permission from Reference [<a href="#B29-nanomaterials-14-01856" class="html-bibr">29</a>]. (<b>c</b>) Stress-strain curves of Al-foil, CNT-P, and CF-CNT-P. Reprinted with permission from Reference [<a href="#B31-nanomaterials-14-01856" class="html-bibr">31</a>]. (<b>d</b>) Schematic of the synthesis process of TNGC material. Reprinted with permission from Reference [<a href="#B39-nanomaterials-14-01856" class="html-bibr">39</a>]. (<b>e</b>) Cycling performance of FVO/rGO and b-FVO materials (500 mAh g<sup>−1</sup>). Reprinted with permission from Reference [<a href="#B40-nanomaterials-14-01856" class="html-bibr">40</a>]. (<b>f</b>) Schematic illustration of the synthesis process of few-layer NbSe<sub>2</sub>@graphene by WBM. Reprinted with permission from Reference [<a href="#B41-nanomaterials-14-01856" class="html-bibr">41</a>]. (<b>g</b>) The cycling performance and corresponding coulombic efficiency of BDT/3DGraphene and BDT at 0.5 C. Reprinted with permission from Reference [<a href="#B44-nanomaterials-14-01856" class="html-bibr">44</a>].</p>
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<p>Other flexible carbon-based materials. (<b>a</b>) The synthesis procedure of Cu/Cu<sub>3</sub>P-N-CNFs current collector and (<b>b</b>) charge and discharge curves of Li-S battery assembled with Cu<sub>3</sub>P-N-CNFs anode. (<b>c</b>) The synthesis procedure of the MP<sub>x</sub>@NC composite materials and (<b>d</b>) rate performance and coulombic efficiency of Ni<sub>2</sub>P@NC//LFP full cell. Reprinted with permission from Reference [<a href="#B51-nanomaterials-14-01856" class="html-bibr">51</a>].</p>
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<p>Flexible lithium anode materials and their properties. (<b>a</b>) The preparation procedure of LMCY. Reprinted with permission from Reference [<a href="#B53-nanomaterials-14-01856" class="html-bibr">53</a>]. (<b>b</b>) The synthesis process of Li/AuCF anode. Reprinted with permission from Reference [<a href="#B56-nanomaterials-14-01856" class="html-bibr">56</a>]. (<b>c</b>) The cycling performance of lithium batteries at 1C of LFP|Cu@Li, LFP|MXene@Li and LFP|MXene@Au@Li. Reprinted with permission from Reference [<a href="#B57-nanomaterials-14-01856" class="html-bibr">57</a>]. (<b>d</b>) Schematic illustration of the process of lithium plating and stripping on MXene@CNF. Reprinted with permission from Reference [<a href="#B58-nanomaterials-14-01856" class="html-bibr">58</a>]. (<b>e</b>) Schematic illustration of lithium metal plating/stripping process on different substrates. (A) Exposed zinc nanosheets and (B) An interface layer with tent shaped nanocavities anchored by Zn-O-C bonds. Reprinted with permission from Reference [<a href="#B59-nanomaterials-14-01856" class="html-bibr">59</a>]. (<b>f</b>) Schematic illustration of LAGP/Li interface modified with rGO/ZnO (GZO). Reprinted with permission from Reference [<a href="#B61-nanomaterials-14-01856" class="html-bibr">61</a>].</p>
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<p>(<b>a</b>) Preparation of flowcharts of PEO-LiTFSI and PEO-PAN-LiTFSI. (<b>b</b>,<b>c</b>) SEM images of (<b>b</b>) the PAN fiber membrane and (<b>c</b>) PEO-PAN-LiTFSI. Reprinted with permission from Reference [<a href="#B66-nanomaterials-14-01856" class="html-bibr">66</a>]. (<b>d</b>) Diagram of wire-shaped cell. (<b>e</b>) (i)–(iv) Photographs of wire-shaped cells in different deformations. Reprinted with permission from Reference [<a href="#B67-nanomaterials-14-01856" class="html-bibr">67</a>]. (<b>f</b>) Schematic illustration for the synthesis of DN-Ionogel. (<b>g</b>) Schematic diagram of a flexible all-solid-state lithium battery and a hybrid interface composition during cycling. (<b>h</b>) The upholstery unit provides a display that powers the optical image of a large LED screen in a variety of conditions such as raw, bent, cut, and stamped. Reprinted with permission from Reference [<a href="#B69-nanomaterials-14-01856" class="html-bibr">69</a>].</p>
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<p>(<b>a</b>) Above: Flowchart of converting discarded clothing acrylic into a flexible wearable device. Bottom: Schematic diagram of the preparation of composite electrolytes from waste acrylic yarn. (<b>b</b>) Demonstration of the flexibility of pouch cells. (<b>c</b>) Flow diagram for the preparation of a solid electrolyte by incorporating f-NbS<sub>2</sub> nanosheets into a SPEEK matrix. (<b>d</b>) Capacitance retention and CE of FSSSC under different folding conditions. Reprinted with permission from Reference [<a href="#B6-nanomaterials-14-01856" class="html-bibr">6</a>].</p>
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<p>(<b>a</b>) Flow diagram of flexible electrode preparation by 3DP technology. (<b>b</b>) Cycling performance of the whole battery in both flat and curved states. Reprinted with permission from Reference [<a href="#B4-nanomaterials-14-01856" class="html-bibr">4</a>]. (<b>c</b>) Schematic illustration of the fabrication process of the 3D-printed TPU-based electrodes. Reprinted with permission from Reference [<a href="#B78-nanomaterials-14-01856" class="html-bibr">78</a>]. (<b>d</b>) Composition and morphological characteristics of retractable cell components, and advantages of retractable cells. Reprinted with permission from Reference [<a href="#B79-nanomaterials-14-01856" class="html-bibr">79</a>]. (<b>e</b>) Schematic diagram of the preparation of flexible Si@C NF using electrospinning technique. (<b>f</b>) Structural diagram of a flexible fiber paper electrode before carbonization. Reprinted with permission from Reference [<a href="#B8-nanomaterials-14-01856" class="html-bibr">8</a>].</p>
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<p>(<b>a</b>) Schematic chart of the fabrication for SiO<sub>x</sub>/E@CPPC. Reprinted with permission from Reference [<a href="#B86-nanomaterials-14-01856" class="html-bibr">86</a>]. (<b>b</b>) Schematic diagram of a stacked thin-film cell configuration. Reprinted with permission from Reference [<a href="#B89-nanomaterials-14-01856" class="html-bibr">89</a>]. (<b>c</b>) Schematic presentation of the simultaneous EPD process before and after application of electric field. Reprinted with permission from Reference [<a href="#B90-nanomaterials-14-01856" class="html-bibr">90</a>]. (<b>d</b>) Schematic diagram of the preparation process of the flexible cathode current collector. Reprinted with permission from Reference [<a href="#B91-nanomaterials-14-01856" class="html-bibr">91</a>]. (<b>e</b>) Overview diagram of electroplating each component of Li-based batteries. Reprinted with permission from Reference [<a href="#B92-nanomaterials-14-01856" class="html-bibr">92</a>]. (<b>f</b>) Schematic illustration of electrodeposition process.</p>
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<p>(<b>a</b>) Schematic diagram of a flexible structure battery for bone and joint bionics. Reprinted with permission from Reference [<a href="#B106-nanomaterials-14-01856" class="html-bibr">106</a>]. (<b>b</b>) Design concept diagram of a battery with flexible structure based on animal vertebrae biomimicry. Reprinted with permission from Reference [<a href="#B107-nanomaterials-14-01856" class="html-bibr">107</a>]. (<b>c</b>) Schematic diagram of the preparation of four CuO/Cu integrated folded electrodes. (<b>d</b>) Schematic diagram of a textile battery module. Reprinted with permission from Reference [<a href="#B114-nanomaterials-14-01856" class="html-bibr">114</a>]. (<b>e</b>) Fabrication process of the zigzag-like foldable battery. Reprinted with permission from Reference [<a href="#B115-nanomaterials-14-01856" class="html-bibr">115</a>]. (<b>f</b>) DNA helix structure and the helix-inspired battery design. Reprinted with permission from Reference [<a href="#B116-nanomaterials-14-01856" class="html-bibr">116</a>].</p>
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15 pages, 5443 KiB  
Article
Carbonaceous Decomposition Products at High Temperatures and Their Interfacial Role in the Friction Behaviour of Composite Brake Material
by Piyush Chandra Verma, Pranesh Aswath, Giovanni Straffelini and Stefano Gialanella
Lubricants 2024, 12(11), 399; https://doi.org/10.3390/lubricants12110399 - 20 Nov 2024
Viewed by 264
Abstract
This study aims to investigate the outcomes of carbonaceous products, derived from the decomposition of the components of vehicular brake materials, under high-temperature wear tests. Pin-on-disc (PoD) wear tests were conducted by using cast iron discs against pins made of commercially available low-steel [...] Read more.
This study aims to investigate the outcomes of carbonaceous products, derived from the decomposition of the components of vehicular brake materials, under high-temperature wear tests. Pin-on-disc (PoD) wear tests were conducted by using cast iron discs against pins made of commercially available low-steel friction material. Tests were carried out at different temperatures: 155 °C, 200 °C, 250 °C, and 300 °C. The characterization of the sliding plateaus on worn pin surfaces was based on X-ray diffraction (XRD), scanning electron microscopy (SEM), and Raman spectroscopy. It was noted that at temperatures above 200 °C, the thermal degradation of the inorganic resin, used as a material binder, occurs. An interesting observation was recorded at 300 °C; the brake pin material’s friction curve showed higher stability despite having an excessive wear rate. However, the brake pin’s specific wear coefficient was higher at this temperature than was observed in the other friction tests. A detailed study of the friction plateaus on the worn-out pins at 300 °C revealed that the decomposed carbon resin product, i.e., the distorted graphite, was widespread over the surface of the pin. Lubricant stabilization can be expected, as established by the observed values of the coefficient of friction (CoF), retaining values within the 0.4–0.6 range, even at high temperatures. Other friction material components may have contributed to the formation of this ubiquitous carbonaceous interface film. Full article
(This article belongs to the Special Issue Recent Advances in High Temperature Tribology)
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<p>(<b>a</b>) Cylindrical shape brake material pin placed on GCI disc. (<b>b</b>) Microstructure of virgin brake material.</p>
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<p>High-temperature wear test rig.</p>
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<p>The evolution of the friction coefficient of brake pad friction material at different temperatures.</p>
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<p>(<b>a</b>) Total wear volume of the worn track on the GCI disc at different elevated temperatures, (<b>b</b>,<b>c</b>) the corresponding 3D profilometer observation of the disc at 155 °C and 300 °C, and (<b>d</b>) the average elemental composition of wear debris on the GCI disc’s surface, as determined using EDXS.</p>
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<p>(<b>a</b>) Specific wear coefficients for brake pad pins in relation to disc temperature. SEM of worn surfaces of brake pad pins at different elevated temperatures: (<b>b</b>) 155 °C, (<b>c</b>) 200 °C, (<b>d</b>) 250 °C, and (<b>e</b>) 300 °C. (<b>f</b>,<b>g</b>) SEM images of loose wear debris collected at 155 °C and 300 °C friction tests.</p>
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<p>(<b>a</b>) Specific wear coefficients for brake pad pins in relation to disc temperature. SEM of worn surfaces of brake pad pins at different elevated temperatures: (<b>b</b>) 155 °C, (<b>c</b>) 200 °C, (<b>d</b>) 250 °C, and (<b>e</b>) 300 °C. (<b>f</b>,<b>g</b>) SEM images of loose wear debris collected at 155 °C and 300 °C friction tests.</p>
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<p>(<b>a</b>) Comparison of XRD spectra acquired on brake pad pin samples at 155 °C, 200 °C, 250 °C, and 300 °C, respectively. (<b>b</b>) Full-profile Rietveld fit using the MAUD software for pin samples at 250 °C.</p>
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<p>(<b>a</b>) A Raman spectroscopic comparison at a worn-out pin surface at various working temperatures. (<b>b</b>) A magnified image of the Raman spectra, with Ca<sub>3</sub>P<sub>2</sub>O<sub>8</sub> at 967 cm<sup>−1</sup>, SnO<sub>2</sub> at 776 cm<sup>−1</sup>, Mg<sub>2</sub>SiO<sub>4</sub> at 790 cm<sup>−1</sup>, and with ND as the corresponding wavelength.</p>
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<p>De-convolution of Raman spectroscopy performed on pin surface at (<b>a</b>) 155 °C, (<b>b</b>) 200 °C, (<b>c</b>) 250 °C, and (<b>d</b>) 300 °C testing temperatures.</p>
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<p>Wear mechanism for friction tests at (<b>a</b>) lower (155–200 °C) and (<b>b</b>) higher temperatures (250–300 °C).</p>
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