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J. Compos. Sci., Volume 9, Issue 2 (February 2025) – 41 articles

Cover Story (view full-size image): Concerns over synthetic fibers’ biodegradability and microplastic pollution have driven the shift toward sustainable textiles. However, natural textiles lack inherent hydrophobicity, limiting their use in technical applications. Traditional hydrophobic coatings rely on PFAS, which pose environmental and health risks. Emerging research focuses on PFAS-free alternatives, yet many remain synthetic. Natural coatings made from natural compounds, such as waxes, fatty acids, naturally occurring polymeric compounds, and other naturally occurring substances, offer a greener solution with a lower environmental footprint. This review examines their hydrophobic efficiency, durability, and scalability, comparing them to PFAS-based coatings. Can nature-derived coatings achieve the performance of synthetic solutions while maintaining sustainability? View this paper
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24 pages, 3469 KiB  
Article
Application of DFT and Experimental Tests for the Study of Compost Formation Between Chitosan-1,3-dichloroketone with Uses for the Removal of Heavy Metals in Wastewater
by Joaquín Alejandro Hernández Fernández, Jose Alfonso Prieto Palomo and Rodrigo Ortega-Torod
J. Compos. Sci. 2025, 9(2), 91; https://doi.org/10.3390/jcs9020091 - 19 Feb 2025
Abstract
The environment presently contains greater amounts of heavy metals due to human activities, causing toxicity, mutagenicity, and carcinogenicity. This study evaluated a chitosan (CS) composite material combined with 1,3-dichlorocetone to extract heavy metals from affected waters, integrating experimental and computational analyses. The synthesis [...] Read more.
The environment presently contains greater amounts of heavy metals due to human activities, causing toxicity, mutagenicity, and carcinogenicity. This study evaluated a chitosan (CS) composite material combined with 1,3-dichlorocetone to extract heavy metals from affected waters, integrating experimental and computational analyses. The synthesis of chitosan, obtained from shrimp waste chitin, reached a yield of 85%. FTIR analysis confirmed key functional groups (NH2 and OH), and XRD showed high crystallinity with peaks at 2θ = 8° and 20°. The physicochemical properties evaluated included a moisture content of 7.3%, ash content of 2.4%, and a deacetylation degree of 73%, consistent with commercial standards. Chitosan exhibited significant solubility in 1.5% acetic acid, moderate solubility in water, and insolubility in NaOH, demonstrating its versatility for environmental applications. In adsorption tests, heavy metal concentrations were reduced by CS derivatives, with Cr and Pb dropping to 0.03 mg/L, and Cu and Zn to less than 0.05 mg/L. CS cross-linked with 1,3-dichlorocetone proved the most efficient, outperforming other derivatives such as glutaraldehyde and epichlorohydrin. Computational analysis evaluated key molecular interactions using DFT and the B3LYP/LANLD2Z method. The band gap energies (HOMO–LUMO) decreased to 0.09753 eV for Zn and 0.01485 eV for Pb, indicating high affinity, while Cd showed lower interaction (0.11076 eV). The total dipole moment increased remarkably for Zn (14.693 Debye) and Pb (7.449 Debye), in contrast to Cd (4.515 Debye). Other descriptors, such as chemical hardness (η), reflected a higher reactivity for Zn (0.04877 eV) and Pb (0.00743 eV), which favors adsorption. The correlation between experimental and computational results validates the efficiency and selectivity of CS/1,3-dichlorocetone for removing heavy metals, especially Pb and Zn. This material stands out for its adsorbent capacity, sustainability, and economic viability, positioning it as a promising solution for wastewater remediation. Full article
(This article belongs to the Special Issue Characterization and Modeling of Composites, 4th Edition)
16 pages, 1006 KiB  
Systematic Review
Composite Dust Toxicity Related to Restoration Polishing: A Systematic Review
by Kamila Kucharska, Anna Lehmann, Martyna Ortarzewska, Jakub Jankowski and Kacper Nijakowski
J. Compos. Sci. 2025, 9(2), 90; https://doi.org/10.3390/jcs9020090 - 18 Feb 2025
Abstract
An integral part of daily dental practice is preparing and polishing placed composite restorations. When these procedures are performed, significant amounts of composite dust are released from the grinding material. This systematic review aims to enhance the existing body of knowledge, encourage further [...] Read more.
An integral part of daily dental practice is preparing and polishing placed composite restorations. When these procedures are performed, significant amounts of composite dust are released from the grinding material. This systematic review aims to enhance the existing body of knowledge, encourage further dialogue, and expand the understanding of composite dust and its related risks. Following inclusion and exclusion criteria, twelve studies were included. Several studies highlight that composite dust contains nanoparticles capable of deep lung penetration, posing significant health risks to both dental staff and patients. Inhalation of composite dust can lead to respiratory diseases such as pneumoconiosis. Studies have shown that water cooling during composite grinding reduces dust emissions but does not eliminate them completely. Researchers suggest that thermal degradation of the composite material, not just filler particles, may be the source of the nanoparticles. In vitro studies have shown the toxicity of composite dust to bronchial and gingival epithelial cells, especially at high concentrations. Further research is needed on the health effects of composite dust and the development of effective methods to protect staff and patients. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
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<p>PRISMA flow diagram presenting search strategy.</p>
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<p>Quality assessment, including the main potential risk of bias (risk level: green—low, yellow—unspecified, red—high; quality score: green—good, yellow—intermediate, red—poor) [<a href="#B14-jcs-09-00090" class="html-bibr">14</a>,<a href="#B17-jcs-09-00090" class="html-bibr">17</a>,<a href="#B18-jcs-09-00090" class="html-bibr">18</a>,<a href="#B19-jcs-09-00090" class="html-bibr">19</a>,<a href="#B20-jcs-09-00090" class="html-bibr">20</a>,<a href="#B30-jcs-09-00090" class="html-bibr">30</a>,<a href="#B31-jcs-09-00090" class="html-bibr">31</a>,<a href="#B32-jcs-09-00090" class="html-bibr">32</a>,<a href="#B33-jcs-09-00090" class="html-bibr">33</a>,<a href="#B34-jcs-09-00090" class="html-bibr">34</a>,<a href="#B35-jcs-09-00090" class="html-bibr">35</a>,<a href="#B36-jcs-09-00090" class="html-bibr">36</a>].</p>
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21 pages, 12291 KiB  
Article
Energy Absorption Mechanisms of Riveted and Assembled Double-Trapezoidal Auxetic Honeycomb Core Structures Under Quasi-Static Loading
by Zhenhua Tian, Shaoqing Shi, Yu Liao, Wenkang Wang, Lei Zhang and Yingjie Xiao
J. Compos. Sci. 2025, 9(2), 89; https://doi.org/10.3390/jcs9020089 - 14 Feb 2025
Abstract
Auxetic honeycomb structures, known for their exceptional mechanical properties, are widely used as sacrificial layers to protect critical targets from extreme explosive loads. However, conventional double arrowhead auxetic honeycomb-core structures (DA-AHSs) encounter significant interfacial connectivity challenges, and scaling auxetic honeycombs with alternative cellular [...] Read more.
Auxetic honeycomb structures, known for their exceptional mechanical properties, are widely used as sacrificial layers to protect critical targets from extreme explosive loads. However, conventional double arrowhead auxetic honeycomb-core structures (DA-AHSs) encounter significant interfacial connectivity challenges, and scaling auxetic honeycombs with alternative cellular microstructures introduces further complexity. To overcome these issues, riveted and assembled double-trapezoidal auxetic honeycomb-core structures (DT-AHSs) were developed as a replacement for DA-AHSs. The deformation modes and energy absorption mechanisms of DT-AHSs were analyzed through theoretical methods and quasi-static testing. The results show that DT-AHSs energy absorption primarily relies on the yield deformation of the longer inclined walls and rotational deformation of the shorter inclined walls. Additionally, the shorter walls support auxetic behavior by stabilizing the deformation of the longer walls. These findings provide a basis for further exploration of the protective potential of DT-AHSs. Full article
(This article belongs to the Section Composites Applications)
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<p>Schematic of honeycomb structure and details of high/low ‘trapezoidal’ riveting variations.</p>
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<p>Simplified diagram of the unit cell model.</p>
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<p>Schematic diagram of unit cell and simplified analysis.</p>
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<p>Specimen diagram after riveting.</p>
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<p>Compression test setup.</p>
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<p>The deformation modes of three honeycomb structures: (<b>a</b>) undeformed state, (<b>b</b>) <span class="html-italic">ε</span> = 0.28, (<b>c</b>) <span class="html-italic">ε</span> = 0.56, (<b>d</b>) fully compressed dense state.</p>
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<p>The deformation diagram of the lateral cells of the structures highlighted in the red box in <a href="#jcs-09-00089-f006" class="html-fig">Figure 6</a>: (<b>a</b>) undeformed state, (<b>b</b>) <span class="html-italic">ε</span> = 0.28, (<b>c</b>) <span class="html-italic">ε</span> = 0.56, (<b>d</b>) fully compressed dense state.</p>
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<p>Nominal stress–strain curves and <span class="html-italic">η</span>–strain curves: (<b>a</b>) DT-AHS, (<b>b</b>) 2D-DHS, (<b>c</b>) CHHS.</p>
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<p>Comparison of energy absorption performance indices.</p>
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<p>The deformation modes of DT-AHSs with different layers: (<b>a</b>) undeformed state, (<b>b</b>) <span class="html-italic">ε</span> = 0.28, (<b>c</b>) <span class="html-italic">ε</span> = 0.56, (<b>d</b>) fully compressed dense state.</p>
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<p>Stress–strain and <span class="html-italic">η</span>–strain curves of DT-AHSs with varying <span class="html-italic">n</span>-values (<b>a</b>) <span class="html-italic">n</span> = 1, (<b>b</b>) <span class="html-italic">n</span> = 2, (<b>c</b>) <span class="html-italic">n</span> = 3, (<b>d</b>) <span class="html-italic">n</span> = 4, (<b>e</b>) <span class="html-italic">n</span> = 5.</p>
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<p>Influence of <span class="html-italic">n</span>-values on energy absorption performance indices.</p>
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<p>The deformation modes of DT-AHSs with different <span class="html-italic">l</span><sub>1</sub>: (<b>a</b>) undeformed state; (<b>b</b>) <span class="html-italic">ε</span> = 0.28; (<b>c</b>) <span class="html-italic">ε</span> = 0.56; (<b>d</b>) fully compressed dense state.</p>
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<p>Nominal stress–strain curves and <span class="html-italic">η</span>–strain curves of DT-AHSs with different <span class="html-italic">l</span><sub>1</sub>: (<b>a</b>) DL1-01, (<b>b</b>) DL1-02, (<b>c</b>) DL1-03, (<b>d</b>) DL1-04.</p>
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<p>Effect of changing <span class="html-italic">l</span><sub>1</sub> on the energy absorption properties.</p>
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<p>The deformation modes of DT-AHS with different <span class="html-italic">l</span><sub>2</sub>: (<b>a</b>) undeformed state, (<b>b</b>) <span class="html-italic">ε</span> = 0.28, (<b>c</b>) <span class="html-italic">ε</span> = 0.56, (<b>d</b>) fully compressed dense state.</p>
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<p>Nominal stress–strain curves and <span class="html-italic">η</span>–strain curves of DT-AHSs with different <span class="html-italic">l</span><sub>2</sub>: (<b>a</b>) DL2-01, (<b>b</b>) DL2-02, (<b>c</b>) DL2-03, (<b>d</b>) DL2-04, (<b>e</b>) DL2-05.</p>
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<p>Effect of changing <span class="html-italic">l</span><sub>2</sub> on the energy absorption properties.</p>
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<p>Effect on SEA of DT-AHSs under comparison: (<b>a</b>) <span class="html-italic">l</span><sub>1</sub> (<span class="html-italic">l</span><sub>2</sub>) value affects SEA, (<b>b</b>) <span class="html-italic">θ</span><sub>1</sub> (<span class="html-italic">θ</span><sub>2</sub>) value affects SEA.</p>
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19 pages, 18754 KiB  
Article
The Design and Characterization of an Artificial Soil Substrate Made from Sand-Washing Slurry
by Biqin Dong, Xu Wu, Penghui Wang, Rongxin Peng and Yanshuai Wang
J. Compos. Sci. 2025, 9(2), 88; https://doi.org/10.3390/jcs9020088 - 13 Feb 2025
Abstract
The global reserve of sand has significantly decreased, and sand washing is predominantly favored due to its simplicity and low operational costs, but this method poses significant environmental risks like landslides, making its reuse essential for sustainability. In view of this challenge, based [...] Read more.
The global reserve of sand has significantly decreased, and sand washing is predominantly favored due to its simplicity and low operational costs, but this method poses significant environmental risks like landslides, making its reuse essential for sustainability. In view of this challenge, based on the composite preparation method, an innovative approach was proposed to prepare an artificial soil substrate from sand-washing slurry. The physical and vegetative feasibility performance, including strength, density, water absorption, retention, electrical conductivity (EC), and pH; and microstructural characteristics, including X-ray diffraction (XRD), scanning electron microscopy (SEM), and nuclear magnetic resonance (NMR) of the artificial soil substrate with different proportions of cement and foaming agent were measured. Increasing the cement content to 30% of un-crushed artificial soil substrate specimens improved strength, whereas 40% reduced it due to the diminished pore-filling effect. Water absorption rates ranged from 29.22% to 36.68%, increasing with more foaming agent and decreasing with more cement, while the water retention time was 12–14 days, and incorporating foaming agent significantly increased water absorption. Leachate pH ranged from 11.99 to 12.18, and reduced to 7.82–8.28 with 5% phosphoric acid. The EC of the artificial soil substrate decreased by 88.64% to 93.59% after 10 wet–dry cycles, aligning with the standard. Artificial-soil-substrate-predominant products include calcite, quartz, and dolomite, with a pronounced silica content and soil substrate porosity ranging from 27.96% to 51.80%. From the microstructural test, calcium silicate hydrate gel, produced by cement hydration, effectively bound the sand-washing slurry, thereby improving strength. Full article
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<p>Raw material morphology: (<b>a</b>) sand-washing slurry; (<b>b</b>) pre-treated sand-washing slurry; (<b>c</b>) cement; (<b>d</b>) foaming agent.</p>
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<p>Particle size distribution, XRD patterns, and SEM image of sand-washing slurry. (<b>a</b>) Particle size distribution. (<b>b</b>) XRD patterns. (<b>c</b>) SEM image.</p>
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<p>The particle size distribution, XRD patterns, and SEM image of sand-washing slurry.</p>
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<p>Compressive strength and average density of different specimens. (<b>a</b>) Compressive strength. (<b>b</b>) Density.</p>
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<p>Percentage of different particle sizes after crushing of artificial soil substrate.</p>
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<p>Water absorption rates of artificial soil substrate particles.</p>
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<p>Time-varying water retention rate of artificial soil substrate particles.</p>
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<p>Effect of different phosphoric acid concentrations on the pH of artificial soil substrate. (<b>a</b>) Change in pH after treatment. (<b>b</b>) Effect of phosphoric acid on pH of S3C7-2.</p>
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<p>EC values of artificial soil substrate with different proportions.</p>
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<p>EC values of artificial soil substrate after 10 wet–dry cycles.</p>
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<p>Percolation rate of the artificial soil substrate with different proportions.</p>
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<p>XRD results of artificial soil substrate particles with different proportions: (<b>a</b>) 80% sand-washing slurry; (<b>b</b>) 70% sand-washing slurry; (<b>c</b>) 60% sand-washing slurry.</p>
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<p>SEM images of artificial soil substrate particles at different level magnifications: (<b>a</b>) 100×; (<b>b</b>) 200×; (<b>c</b>) 500×; (<b>d</b>) 2000×; (<b>e</b>) 2000×; (<b>f</b>) 4000×; (<b>g</b>) 10,000×.</p>
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<p>The porosity of the artificial soil substrate with different proportions.</p>
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<p>Pore size distribution of artificial soil substrate with different proportions: (<b>a</b>) sample S8C2; (<b>b</b>) sample S7C3; (<b>c</b>) sample S6C4.</p>
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<p>Small-scale planting experiments.</p>
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11 pages, 5433 KiB  
Article
Thermodynamic Analysis on Complex Oxides Formed by Aerodynamic Heating for Ultrahigh-Temperature Ceramic Matrix Composites
by Mizuki Tsuganezawa, Yutaro Arai and Ryo Inoue
J. Compos. Sci. 2025, 9(2), 87; https://doi.org/10.3390/jcs9020087 - 13 Feb 2025
Abstract
The oxidation and recession of carbon-fiber-reinforced ultrahigh-temperature ceramic matrix composites (C/UHTCMCs) fabricated via reactive melt infiltration (RMI) using Zr-Ti alloys with three different compositions are evaluated via an arc-jet tunnel test at temperatures above 2000 °C for 60 s. Thermodynamic evaluations show that [...] Read more.
The oxidation and recession of carbon-fiber-reinforced ultrahigh-temperature ceramic matrix composites (C/UHTCMCs) fabricated via reactive melt infiltration (RMI) using Zr-Ti alloys with three different compositions are evaluated via an arc-jet tunnel test at temperatures above 2000 °C for 60 s. Thermodynamic evaluations show that the recession of the UHTCMCs is prevented by the formation of a solid solution of ZrTiO4 on their exposed surface. Because an increase in the Zr content increases the melting temperature of ZrTiO4, the recession of the composites increases as the Zr content in the infiltrated alloys decreases. UHTCMCs fabricated with Zr-20at%Ti showed the least recession (<5%). Full article
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<p>Typical microstructures of C/C preform: (<b>a</b>) in-plane direction, (<b>b</b>) through-the-thickness direction [<a href="#B50-jcs-09-00087" class="html-bibr">50</a>].</p>
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<p>Typical microstructures for prepared composites: (<b>a</b>) Z20, (<b>b</b>) Z36, and (<b>c</b>) Z80 [<a href="#B50-jcs-09-00087" class="html-bibr">50</a>].</p>
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<p>XRD analyses for prepared composites [<a href="#B50-jcs-09-00087" class="html-bibr">50</a>].</p>
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<p>Temperature profiles during the arc-wind tunnel test.</p>
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<p>The appearance of the surface after the arc-wind tunnel test: (<b>a</b>) C/C, (<b>b</b>) Z20, (<b>c</b>) Z36, and (<b>d</b>) Z80.</p>
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<p>The typical microstructures of the exposed surface obtained by SEM: (<b>a</b>) Z20, (<b>b</b>) Z36, and (<b>c</b>) Z80.</p>
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<p>The cross-sections of the composites with EDS mapping for the C, O, Zr, and Ti element after the arc-wind tunnel test: (<b>a</b>) Z20, (<b>b</b>) Z36, and (<b>c</b>) Z80.</p>
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<p>Relationship between the Zr content in the infiltrated alloy and the normalized thickness of the specimen (the circular symbols represent the plots of the test after 60 and 30 s, respectively) [<a href="#B50-jcs-09-00087" class="html-bibr">50</a>].</p>
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<p>Volatility diagram of the TiC-ZrC system at 2000 °C.</p>
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14 pages, 4163 KiB  
Article
Non-Destructive Evaluation of Impact-Damaged Sandwich Composites: Influence of Fiber Type
by Jaime Santos, Paulo N. B. Reis, Mario Santos and Ana M. Amaro
J. Compos. Sci. 2025, 9(2), 86; https://doi.org/10.3390/jcs9020086 - 12 Feb 2025
Abstract
This study deals with the evaluation of impact-damaged sandwich composites using different fiber types (carbon, glass, and Kevlar), where the outer layers, or “skins”, were made from the same type of fiber, while the inner layer, or “core”, consisted of a different fiber [...] Read more.
This study deals with the evaluation of impact-damaged sandwich composites using different fiber types (carbon, glass, and Kevlar), where the outer layers, or “skins”, were made from the same type of fiber, while the inner layer, or “core”, consisted of a different fiber type, with the aim of improving the damage resistance and tolerance of composite materials. To achieve this goal, the following research question was formulated: can the type of core fiber used in sandwich composites primarily determine their structural response under impact? To obtain a consolidated answer, various configurations manufactured were subjected to low-velocity impact tests to induce damage. The next step involved evaluating the extent and distribution of damage across various samples using ultrasonic C-scan techniques, along with assessing the impact bending stiffness (IBS) property, a widely recognized method for measuring the structural response of composites. It was observed that the different composite configurations presented distinct absorbed energy and, consequently, different damages, which was confirmed by the IBS and the C-scan methods. The glass–carbon–glass (GCG) sandwich composite demonstrated superior performance in mitigating damage compared to the other sandwich designs. The core material was verified as the main factor influencing the response of the sandwich composite. Full article
(This article belongs to the Special Issue Recent Progress in Hybrid Composites)
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<p>(<b>a</b>) Dimensions of the specimens (in mm); (<b>b</b>) aspect of the cross-sectional view of Kevlar specimens; (<b>c</b>) aspect of the cross-sectional view of CGC specimens.</p>
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<p>Immersion C-scan.</p>
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<p>Air-coupling C-scan.</p>
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<p>Energy–time curves for composites with single fiber.</p>
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<p>Load–displacement curve for all composites with single fiber.</p>
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<p>Damage images for the carbon sample with a single fiber: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm).</p>
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<p>Damage images for the Kevlar sample with a single fiber: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm); (<b>c</b>) 3D image.</p>
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<p>Carbon sample: (<b>a</b>) front damage; (<b>b</b>) back damage.</p>
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<p>Damage image for the glass sample with a single fiber by air-coupling C-scan (xx = 40 mm; yy = 50 mm).</p>
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<p>Damage images for the carbon–glass–carbon sample: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm).</p>
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<p>Damage images for the glass–carbon–glass sample: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm); (<b>c</b>) 3D image.</p>
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<p>Damage images for the glass–carbon–glass sample: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm); (<b>c</b>) 3D image.</p>
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<p>Damage images for the glass–Kevlar–glass sample: (<b>a</b>) air-coupling C-scan (xx = 40 mm; yy = 50 mm); (<b>b</b>) immersion C-scan (xx = 50 mm; yy = 50 mm).</p>
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12 pages, 2555 KiB  
Article
Highly Stable and Temperature-Independent Humidity Sensor Based on PEO/PVA Polymer Composite
by H. M. Zeeshan Yousaf, Mazhar Javed, Muhammad Mehran Bashir, Rayyan Ali Shaukat and Hasan Mahmood
J. Compos. Sci. 2025, 9(2), 85; https://doi.org/10.3390/jcs9020085 - 12 Feb 2025
Abstract
Traditional humidity sensors frequently face challenges, especially in environments with fluctuating temperatures, which can compromise their efficiency, stability, and reliability. Therefore, there is an urgent demand to fabricate low-cost and high-performance temperature-independent humidity sensors. In this work, for the first time, highly stable [...] Read more.
Traditional humidity sensors frequently face challenges, especially in environments with fluctuating temperatures, which can compromise their efficiency, stability, and reliability. Therefore, there is an urgent demand to fabricate low-cost and high-performance temperature-independent humidity sensors. In this work, for the first time, highly stable and reliable temperature-independent humidity sensors have been proposed based on a PEO/PVA polymer composite. Four sensors were fabricated containing weight ratios of PEO/PVA as 50:50%, 40:60%, 60:40%, and 70:30%, respectively. All of the fabricated sensors were electrically characterized at three different temperatures, 30 °C, 35 °C, and 40 °C, to investigate the impedance response. The proposed sensor based on a PEO/PVA (40:60%) composite presents a remarkable and optimized temperature-independent performance in the range of 0–60%RH. Apart from this, the response and recovery time (9 s/16 s) of the temperature-independent humidity sensor based on PEO/PVA (40:60%) were investigated. Finally, the sensor showed long-term stability for 90 days, ensuring the reliability of the proposed device. These remarkable performances of the proposed sensor based on PEO/PVA with a weight ratio of (40:60)% can open a new gateway for low-range temperature-independent humidity sensors for various real-time applications. Full article
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<p>Schematic representation of the preparation of the PEO/PVA polymer-composite-based active layer and fabrication of humidity sensor.</p>
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<p>Detailed schematic of the automatic humidity and temperature measurement setup with controlled environment chamber and auto data logging.</p>
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<p>(<b>a</b>–<b>c</b>) SEM image of PEO/PVA (40:60%) polymer composite at the magnification of 20 µm, 10 µm, and 50 µm; (<b>d</b>) EDS mapped image; (<b>e</b>) C K series; O K series and Si K series; (<b>f</b>) atomic weight percentage and elemental analysis of PEO/PVA (40:60%) polymer composite; and (<b>g</b>) FTIR spectrum of PEO/PVA (40:60%) polymer composite.</p>
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<p>Impedance response of the sensors with PEO/PVA with different concentrations: (<b>a</b>) 40:60, (<b>b</b>) 60:64, (<b>c</b>) 50:50, (<b>d</b>) 70:30, and (<b>e</b>) hysteresis curve of the PEO/PVA (40:60) polymer-composite-based temperature-independent humidity sensor.</p>
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<p>(<b>a</b>) Reproducibility of the PEO/PVA (40:60) polymer-composite-based temperature-independent humidity sensor; (<b>b</b>) reproducibility of the PEO/PVA (60:40) polymer-composite-based temperature-independent humidity sensor; (<b>c</b>) response and recovery time of the PEO/PVA (40:60) polymer-composite-based temperature-independent humidity sensor; and (<b>d</b>) repeated cycles of the response and recovery time of the PEO/PVA (40:60) polymer-composite-based temperature-independent humidity sensor.</p>
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16 pages, 3202 KiB  
Article
Kinetic Analysis of the Cracking Behavior in Methanol-Treated Poly(methyl methacrylate)/Functionalized Graphene Composites
by Bing-Hong Yang, Shou-Yi Chang, Yulin Zhang, Fuqian Yang and Sanboh Lee
J. Compos. Sci. 2025, 9(2), 84; https://doi.org/10.3390/jcs9020084 - 11 Feb 2025
Abstract
Structural degradation in liquid environments can hinder the applications of polymer composites as structural materials. In this work, we study the impacts of methanol on surface cracking and the propagation of pre-formed cracks in UV-irradiated poly(methyl methacrylate)/functionalized graphene (PMMA/FG) composites, followed by the [...] Read more.
Structural degradation in liquid environments can hinder the applications of polymer composites as structural materials. In this work, we study the impacts of methanol on surface cracking and the propagation of pre-formed cracks in UV-irradiated poly(methyl methacrylate)/functionalized graphene (PMMA/FG) composites, followed by the uptake of three different crack-generated solvents, namely 1-butanol, cyclohexanol, and 2EA, respectively. The density of surface cracks increases with the increase in the uptake of the crack-generated solvent. The dependence of the nominal diffusivity for the surface cracking on temperature follows an Arrhenius-like law. The methanol in the composites enhances the uptake of the crack-generated solvent, accompanied by the desorption of methanol, and accelerates the initiation and propagation of surface cracks. The activation energy for the initiation of surface cracks shows an increasing dependence on the Hansen solubility distance from methanol. The progression of the pre-formed crack length with time follows a parabolic law. The nominal diffusivity of the crack-generated solvent for the propagation of the single-crack is greater in the healing zone than in the crack-free zone; the corresponding activation energies exhibit an opposite trend. Increasing the fraction of functionalized graphene and decreasing the UV-irradiation dose cause increases in the energy barriers that need to be overcome for the surface cracking and propagation of preexisting cracks. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
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<p>(<b>a</b>) Optical images of a PMMA/0.3-FG composite that was initially submerged in methanol at 50 °C for 25 min, followed by immersion in 1-butanol for different times; optical images of the sizes of a crack grown from a pre-formed crack in an unirradiated, incompletely healed PMMA at different instances after being immersed in 2EA at 30 °C, which was immersed first in methanol at 30 °C for 3 min: (<b>b</b>) in a healed zone and (<b>c</b>) in the non-healed zone.</p>
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<p>(<b>a</b>) Optical images of a PMMA/0.3-FG composite that was initially submerged in methanol at 50 °C for 25 min, followed by immersion in 1-butanol for different times; optical images of the sizes of a crack grown from a pre-formed crack in an unirradiated, incompletely healed PMMA at different instances after being immersed in 2EA at 30 °C, which was immersed first in methanol at 30 °C for 3 min: (<b>b</b>) in a healed zone and (<b>c</b>) in the non-healed zone.</p>
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<p>Time dependence of the surface crack density in PMMA/0.3-FG composites with and without UV irradiation: (<b>a</b>) 0 J/cm<sup>2</sup>, (<b>b</b>) 36.36 J/cm<sup>2</sup>, and (<b>c</b>) 54.54 J/cm<sup>2</sup>. The PMMA/0.3-FG composites were placed first in methanol at 50 °C for 25 min and then in 2EA at respective temperatures of 20, 30, 40, and 50 °C.</p>
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<p>Time dependence of the crack sizes of partially healed cracks in PMMA/0.7-FG composites subjected to (<b>a</b>) 0 J/cm<sup>2</sup>, (<b>b</b>) 36.36 J/cm<sup>2</sup>, and (<b>c</b>) 54.54 J/cm<sup>2</sup> of UV irradiation. The PMMA/0.7-FG composites were submerged in the solvent of 1-butanol after being placed first in methanol to heal the preexisting cracks partially. Note that symbols orange diamond, green triangle, blue round, red round, and blue inverted triangle represent data for 45, 40, 35, 30, and 50 °C, respectively. Solid and hollow symbols stand for healing and non-cracked areas.</p>
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<p>Time dependence of the solvent residing in the PMMA/0.7-FG composites, which were UV-irradiated at the dose of 36.36 J/cm<sup>2</sup> and immersed in different desorption liquids at temperatures of (<b>a</b>) 30 °C, (<b>b</b>) 40 °C, (<b>c</b>) 50 °C, and (<b>d</b>) 60 °C.</p>
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<p>Time dependence of the solvent residing in the PMMA/0.7-FG composites, which were UV-irradiated at the dose of 36.36 J/cm<sup>2</sup> and immersed in different desorption liquids at temperatures of (<b>a</b>) 30 °C, (<b>b</b>) 40 °C, (<b>c</b>) 50 °C, and (<b>d</b>) 60 °C.</p>
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<p>Temperature dependence of nominal diffusivities for the surface cracking in PMMA/0.7-FG composites with and without UV irradiation. The PMMA/0.7-FG composites were immersed first in methanol at the temperature of 50 °C for 25 min and then in (<b>a</b>) cyclohexanol, (<b>b</b>) 2EA, and (<b>c</b>) 1-butanol.</p>
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<p>Variation in the activation energy with UV-irradiation dose for the PMMA/<span class="html-italic">n</span>-FG composites placed first in the solvent of methanol over a period of 25 min at the temperature of 50 °C, followed by respective immersions in (<b>a</b>) cyclohexanol, (<b>b</b>) 2EA, (<b>c</b>) 1-butanol (at low temperatures), and (<b>d</b>) 1-butanol (at high temperatures).</p>
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<p>Variation in the activation energy with UV-irradiation dose for the PMMA/<span class="html-italic">n</span>-FG composites placed first in the solvent of methanol over a period of 25 min at the temperature of 50 °C, followed by respective immersions in (<b>a</b>) cyclohexanol, (<b>b</b>) 2EA, (<b>c</b>) 1-butanol (at low temperatures), and (<b>d</b>) 1-butanol (at high temperatures).</p>
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<p>Variation in the activation energy with the UV dose for the propagation of the preexisting cracks in the methanol-treated PMMA/<span class="html-italic">n</span>-FG composites in (<b>a</b>) 2EA, (<b>b</b>) cyclohexanol, and (<b>c</b>) 1-butanol.</p>
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<p>Dependence of the activation energy associated with the incubation time on the UV-irradiation dose for the propagation of the pre-formed cracks in the partially healed region of methanol-treated PMMA/<span class="html-italic">n</span>-FG composites in (<b>a</b>) 2EA, (<b>b</b>) cyclohexanol, and (<b>c</b>) 1-butanol.</p>
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17 pages, 4866 KiB  
Article
Polymer-Derived Carbon Matrix Composites with Boron Nitride Nanotube Reinforcement
by Okunzuwa Austine Ekuase, Qiang Wu, Jin Gyu Park, Jizhe Cai, Zhiyong Liang and Zhibin Yu
J. Compos. Sci. 2025, 9(2), 83; https://doi.org/10.3390/jcs9020083 - 11 Feb 2025
Abstract
This study explored the use of boron nitride nanotubes (BNNTs) as reinforcing fillers to enhance the mechanical properties of polymer-derived carbon matrix composites. BNNT-reinforced carbon matrix composites containing 0.5–5 wt% BNNTs were fabricated with pyrolysis conducted at different temperatures. X-ray diffraction and Raman [...] Read more.
This study explored the use of boron nitride nanotubes (BNNTs) as reinforcing fillers to enhance the mechanical properties of polymer-derived carbon matrix composites. BNNT-reinforced carbon matrix composites containing 0.5–5 wt% BNNTs were fabricated with pyrolysis conducted at different temperatures. X-ray diffraction and Raman spectroscopy revealed enhanced crystallinity and reduced defects in carbon matrix composites with BNNT addition. At 1200 °C pyrolysis temperature, sample shrinkage decreased from 28% in the control sample without BNNT addition to 12% with 5 wt% BNNTs, demonstrating BNNTs’ significant influence on the matrix. The density increased by 20.1% with 5 wt% BNNTs. Mechanical testing demonstrated an enhancement in the failure strain from 0.7% to 0.8% and an 87.8% increase in the work of fracture with 5 wt% BNNTs. Furthermore, the flexural strength and modulus improved by 68.7% and 55.6%, respectively, at this BNNT concentration. Increasing the pyrolysis temperature to 1500 °C further boosted the mechanical properties, with the flexural strength increasing by 283.7% and the flexural modulus by 528.6% when comparing samples containing 5 wt% BNNTs to those without BNNT reinforcement. Samples processed at 1500 °C with 5 wt% BNNT composition exhibited optimal performance. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
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<p>(<b>a</b>) BNNT puffball; (<b>b</b>) BNNT/THF dispersed suspension; (<b>c</b>) BNNT/phenolic/THF solution; (<b>d</b>) prepared 1 wt% BNNT-reinforced carbon composite thin film; (<b>e</b>) after 200 °C post-cure; and (<b>f</b>) after 1200 °C pyrolysis.</p>
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<p>(<b>a</b>) Raman spectroscopy spectra of BNNT-reinforced carbon composites with different BNNT wt% concentrations undergoing pyrolysis at 1200 °C. Deconvolutionized curves are shown for (<b>b</b>) 0.5 wt%; (<b>c</b>) 1 wt%; and (<b>d</b>) 5 wt% BNNTs.</p>
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<p>XRD patterns of (<b>a</b>) BNNT-reinforced carbon matrix composites with different wt% concentrations and pyrolyzed at 1200 °C and (<b>b</b>) pure BNNT.</p>
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<p>SEM and TEM images of carbon matrix composites reinforced with (<b>a</b>) 0 wt%; (<b>b</b>) 0.5 wt%; and (<b>c</b>) 1 wt% and (<b>d</b>) 5 wt% BNNTs heat-treated at 1200 °C. HRTEM images of 5 wt% of BNNTs in carbon matrix composites at (<b>e</b>) 100 nm and (<b>f</b>) 20 nm.</p>
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<p>EDS maps of fracture surfaces of BNNT carbon matrix composites showing homogeneous dispersion of BNNTs.</p>
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<p>(<b>a</b>) Linear shrinkage and (<b>b</b>) density of carbon reinforced with different BNNT wt% heat-treated at 1200 °C.</p>
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<p>(<b>a</b>) Stress–strain curves; (<b>b</b>) flexural modulus; (<b>c</b>) flexural strength; and (<b>d</b>) work of fracture of carbon reinforced with different wt% BNNTs heat-treated at 1200 °C.</p>
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<p>(<b>a</b>) Stress–strain curves; (<b>b</b>) flexural modulus; (<b>c</b>) flexural strength; and (<b>d</b>) work of fracture of carbon reinforced with difference wt% BNNTs heat-treated at 1500 °C.</p>
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<p>FTIR spectra of pure carbon and 5 wt% BNNTs composite heat-treated at 1200 °C and 1500 °C.</p>
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14 pages, 5400 KiB  
Article
Graphene Oxide–Antibiotic Coatings with Improved Resistance to Microbial Colonization for Arthroplasty Implants
by Gheorghe Iosub, Adelina-Gabriela Niculescu, Valentina Grumezescu, Gabriela Dorcioman, Oana Gherasim, Valentin Crăciun, Dragoș Mihai Rădulescu, Alexandru Mihai Grumezescu, Miruna Silvia Stan, Sorin Constantinescu, Alina Maria Holban and Adrian-Radu Rădulescu
J. Compos. Sci. 2025, 9(2), 82; https://doi.org/10.3390/jcs9020082 - 10 Feb 2025
Abstract
In this study, we investigated the biocompatibility and antibacterial efficiency of hydroxyapatite/graphene oxide/ceftazidime (HAp/GO/CFZ) coatings obtained by the Matrix-Assisted Pulsed Laser Evaporation (MAPLE) technique for arthroplasty implants. The coatings were evaluated for their ability to inhibit biofilm formation by model opportunistic pathogens, specifically [...] Read more.
In this study, we investigated the biocompatibility and antibacterial efficiency of hydroxyapatite/graphene oxide/ceftazidime (HAp/GO/CFZ) coatings obtained by the Matrix-Assisted Pulsed Laser Evaporation (MAPLE) technique for arthroplasty implants. The coatings were evaluated for their ability to inhibit biofilm formation by model opportunistic pathogens, specifically Gram-positive Staphylococcus aureus and Gram-negative Escherichia coli, for 24, 48, and 72 h. A significant reduction in the biofilm formation was demonstrated by coating surfaces, which led to a diminution of approximately 4 logs in the CFU/mL values compared to controls. These findings suggested that HAp/GO/CFZ coatings have the potential to prevent infections associated with arthroplasty implants, thereby improving patient outcomes and implant longevity. Full article
(This article belongs to the Special Issue Advances in Laser Fabrication of Composites)
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<p>ATR-FTIR spectra of HAp/GO/CFZ DC and MAPLE coatings obtained at different laser fluences.</p>
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<p>Typical SEM micrographs of HAp/GO/CFZ coatings obtained by MAPLE at (<b>a<sub>1</sub></b>) 300, (<b>b<sub>1</sub></b>) 400, and (<b>c<sub>1</sub></b>) 500 mJ/cm<sup>2</sup> laser fluences, and the corresponding EDS spectra (<b>a<sub>2</sub></b>,<b>b<sub>2</sub></b>,<b>c<sub>2</sub></b>).</p>
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<p>SEM micrographs with corresponding EDS maps of HAp/GO/CFZ coatings obtained by MAPLE at different laser fluences.</p>
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<p>XRD patterns for HAp/GO/CFZ coatings obtained at 500 mJ/cm<sup>2.</sup>.</p>
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<p>Cell viability (MTT assay) and LDH release levels of human fetal osteoblasts after 72 h (results are calculated as means ± standard deviation of three independent experiments and shown relative to control; * <span class="html-italic">p</span> &lt; 0.05 compared to control).</p>
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<p>Morphology of human fetal osteoblasts after 72 h of incubation by cytoskeleton staining (green: F-actin filaments labeled with FITC, and blue: nuclei labeled (with DAPI), where (<b>a</b>) control; (<b>b</b>) reference; (<b>c</b>) HAp/GO/CFZ coated surfaces (500 mJ/cm<sup>2</sup> laser fluence).</p>
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<p>Graphic representation of <span class="html-italic">S. aureus</span> and <span class="html-italic">E. coli</span> biofilm development on HAp/GO/CFZ-coated surfaces (500 mJ/cm<sup>2</sup> laser fluence) compared to uncoated control.</p>
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48 pages, 7112 KiB  
Review
Biobased Hydrophobic Solutions for Natural Textiles—Moving Beyond PFAS
by Petra Jerič, Blaž Likozar and Uroš Novak
J. Compos. Sci. 2025, 9(2), 81; https://doi.org/10.3390/jcs9020081 - 10 Feb 2025
Abstract
In order to achieve hydrophobic properties in textiles, per- and poly-fluoroalkyl substances (PFAS) are often used. These chemicals represent a class of synthetic compounds that have found wide application in numerous industries because of their advantageous properties, such as hydrophobicity, lipophobicity, chemical inertness, [...] Read more.
In order to achieve hydrophobic properties in textiles, per- and poly-fluoroalkyl substances (PFAS) are often used. These chemicals represent a class of synthetic compounds that have found wide application in numerous industries because of their advantageous properties, such as hydrophobicity, lipophobicity, chemical inertness, remarkable lubricity, non-stickiness, exceptional fire resistance, resistance to high temperatures, and high resistance to various weathering conditions. However, recent scientific research has demonstrated that these compounds possess persistent, accumulative, and highly mobile properties that make them an environmental hazard. Since the toxicity of PFAS is now recognized, ongoing research has been initiated to explore new substitutes. This comprehensive review focuses on the exploration of natural-based hydrophobic coatings for natural textiles, which include materials such as natural waxes, fatty acids, naturally occurring polymeric compounds (including proteins, carbohydrates, complex aromatic polymers, and polymers like natural rubber), and other naturally occurring substances. The role of each compound in the hydrophobic coating is also highlighted. This review aims to evaluate the potential of natural compounds as viable replacements for PFAS, focusing on their efficiency and durability. Full article
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<p>PFAS compounds and their accumulative, persistent, hazardous, and mobile properties.</p>
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<p>PFAS life cycle and their environmental and health consequences.</p>
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<p>The role of natural compounds in hydrophobic coatings.</p>
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<p>The behavior of a water droplet on high-surface- and low-surface-energy materials.</p>
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<p>The importance of surface roughness for superhydrophobicity.</p>
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<p>Schematic of a binder.</p>
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<p>Natural compounds used in hydrophobic coatings for natural textiles.</p>
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<p>Deposition of natural wax via layer-by-layer (LBL) self-assembly technique, according to Forsman et al. [<a href="#B12-jcs-09-00081" class="html-bibr">12</a>].</p>
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<p>Molecular structure of stearic acid.</p>
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<p>Oil–water separation efficiency in relation to WCA.</p>
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<p>Deposition of CNCs and chitosan via the pad-dry-curing method, as described by Yang et al. [<a href="#B78-jcs-09-00081" class="html-bibr">78</a>].</p>
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<p>Chemical structure of starch.</p>
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<p>Relationship between WCA and SA.</p>
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<p>Examples of the molecular structures of proteins (zein and casein).</p>
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<p>Molecular structure of resin and natural rubber.</p>
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<p>Examples of molecular structures of naturally occurring compounds.</p>
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<p>Tannin deposition on cotton through immersion followed by laser ablation as described by Tian et al. [<a href="#B51-jcs-09-00081" class="html-bibr">51</a>].</p>
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<p>(<b>Left</b>) Initial WCAs and WCAs after washing, chemical and abrasion durability. (<b>Right</b>) Change in the mechanical properties and air permeability when compared untreated material with treated one.</p>
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14 pages, 4932 KiB  
Article
Metallic Multimaterials Fabricated by Combining Additive Manufacturing and Powder Metallurgy
by Mayank Kumar Yadav, Riddhi Shukla, Lixia Xi, Zhi Wang and Konda Gokuldoss Prashanth
J. Compos. Sci. 2025, 9(2), 80; https://doi.org/10.3390/jcs9020080 - 10 Feb 2025
Abstract
Nature has created a unique combination of materials, and the design and material compositions used in nature are not successfully employed for industrial applications. Metallic multimaterials (MMMs) are a unique class of materials that combine the properties of various metallic constituents (both matrix [...] Read more.
Nature has created a unique combination of materials, and the design and material compositions used in nature are not successfully employed for industrial applications. Metallic multimaterials (MMMs) are a unique class of materials that combine the properties of various metallic constituents (both matrix and reinforcement(s)) to improve the functionality, performance in real-time, and application spectrum. Accordingly, this study explores the fabrication perspective of MMMs by combining both additive manufacturing (AM) and powder metallurgical (PM) routes. Ti6Al4V structures were fabricated via the laser powder-bed fusion (LPBF) process, and the reinforcement powders were added into the spark plasma sintering (SPS) mold where the Ti6Al4V structures were placed. Different reinforcement compositions including Mg, Al, Fe, Ni, and Cu were explored. Since the present study is focused on the variation of hardness, the hardness profile of the MMM composite was explored showing a sinusoidal trend. This study stands as a testimonial of fabricating MMM composites via a combination of AM and PM processes. Full article
(This article belongs to the Special Issue Metal Composites, Volume II)
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<p>Schematic illustration of the composite manufacturing process: (<b>a1</b>) additive manufacturing of the lattice using LPBF process, (<b>a2</b>) fabricated metal lattice precursor, (<b>b1</b>) spark plasma sintering of the composite by placing the precursor inside the spark plasma sintering mold, and (<b>c1</b>) structure of the fabricated metallic bimetal.</p>
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<p>Scanning electron microscopy–energy dispersive spectroscopy area maps showing the individual constituents present in the metallic multimaterials (MMMs): (<b>a</b>) Ti6Al4V-Mg MMM composite—bimetal composite, (<b>b</b>) Ti6Al4V-Mg-Al composite—trimetal composite, and (<b>c</b>) Ti6Al4V-Mg-Ti-Fe composite—multimaterial composite.</p>
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<p>X-ray diffraction patterns of the different metallic multimaterial composites fabricated by the combination of additive manufacturing and powder metallurgical processes.</p>
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<p>Scanning electron microscopy images (both secondary electron (BE) and back-scattered (BSD) modes) showing the microstructure of the Ti6Al4V–Mg–Al–Fe metallic multimaterial composite.</p>
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<p>Hardness profile plot observed for the Ti6Al4V–Mg–Al–Fe metallic multimaterial composite fabricated by combining additive manufacturing and powder metallurgical processes.</p>
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<p>Scanning electron microscopy–energy dispersive spectroscopy area maps showing the individual constituents present in the 316L SS–Ti–Cu–Ni metallic multimaterial composite.</p>
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22 pages, 6852 KiB  
Article
Experimental Assessment of the Strength and Microstructural Properties of Fly Ash-Containing Basalt Fiber-Reinforced Self-Compacting Sustainable Concrete
by Ala Abu Taqa, Usama A. Ebead, Mohamed O. Mohsen, Mervat O. Aburumman, Ahmed Senouci, Walid Maherzi and Deya Qtiashat
J. Compos. Sci. 2025, 9(2), 79; https://doi.org/10.3390/jcs9020079 - 9 Feb 2025
Abstract
This study investigates the influence of basalt fiber on the rheological, mechanical, and microstructural properties of sustainable self-compacting concrete (SCC) incorporating fly ash and microsilica as supplementary cementitious materials (SCMs). Various SCC mixes were prepared, incorporating five different volume fractions of basalt fiber [...] Read more.
This study investigates the influence of basalt fiber on the rheological, mechanical, and microstructural properties of sustainable self-compacting concrete (SCC) incorporating fly ash and microsilica as supplementary cementitious materials (SCMs). Various SCC mixes were prepared, incorporating five different volume fractions of basalt fiber (0.05%, 0.1%, 0.5%, 1%, and 1.5%), along with a control mix. The rheological properties of fresh SCC were evaluated using slump flow and V-funnel flow tests. Subsequently, the mechanical properties, including compressive strength, splitting tensile strength, and flexural strength, were measured after 28 days of curing. Additionally, microstructural analysis was conducted using scanning electron microscopy (SEM) on fractured specimen surfaces. The results indicated that the inclusion of basalt fiber adversely affected the flowability of fresh SCC mixes, with increased fiber volume. However, the hardened concrete exhibited significant improvements in mechanical properties with the addition of basalt fibers. The optimal performance was observed in the SCC70-85/0.10 mix specimens, which demonstrated a 69.90% improvement in flexural strength and a 23.47% increase in splitting tensile strength compared with the control specimen. SEM analysis further revealed enhanced microstructural density in the concrete matrix containing basalt fiber. A two-factor analysis of variance (ANOVA) with repetitions was conducted to evaluate the effects of varying basalt fiber concentrations on the compressive, flexural, and tensile strengths of SCC mixes. The ANOVA results indicated significant effects for both SCC grade and basalt fiber concentration, demonstrating that each factor independently affected the compressive, tensile, and flexural strengths of SCC. These findings suggest that the incorporation of basalt fibers holds promise for extending building lifespans and enhancing concrete quality, representing a valuable advancement in structural engineering applications. Full article
(This article belongs to the Special Issue Novel Cement and Concrete Materials)
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<p>Mix bleeding.</p>
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<p>Slump flow test.</p>
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<p>V-funnel test.</p>
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<p>SCC specimen mixing, casting, and curing.</p>
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<p>Slump values for concrete mixtures.</p>
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<p>V-funnel values for concrete mixtures.</p>
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<p>Temperature values for concrete mixtures.</p>
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<p>Compressive strength results at 28 days.</p>
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<p>Flexural strength results at 28 days.</p>
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<p>Split-tension strength results at 28 days.</p>
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<p>SEM images of mix 40–55/0.00, (<b>a</b>) Scale 2 mm; (<b>b</b>) Scale 50 µm.</p>
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<p>SEM images of mix 40–55/0.10, (<b>a</b>) Scale 2 mm; (<b>b</b>) Scale 100 µm.</p>
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22 pages, 13197 KiB  
Article
Effects of Polyphosphoric Acid on Physical, Rheological, and Chemical Properties of Styrene-Butadiene-Styrene (SBS)-Modified Asphalt Binder
by Amjad H. Albayati, Mazen J. Al-Kheetan, Aliaa F. Al-ani, Yu Wang, Ahmed M. Mohammed and Mustafa M. Moudhafar
J. Compos. Sci. 2025, 9(2), 78; https://doi.org/10.3390/jcs9020078 - 9 Feb 2025
Abstract
High temperatures combined with heavy traffic load necessitate asphalt binder modification to enhance its performance and durability. This research examines the effects of polyphosphoric acid (PPA) on the physical, rheological, and chemical properties of styrene-butadiene-styrene (SBS)-modified asphalt binders. Asphalt binders were prepared by [...] Read more.
High temperatures combined with heavy traffic load necessitate asphalt binder modification to enhance its performance and durability. This research examines the effects of polyphosphoric acid (PPA) on the physical, rheological, and chemical properties of styrene-butadiene-styrene (SBS)-modified asphalt binders. Asphalt binders were prepared by adding 3% SBS and varying PPA dosages of 0.3%, 0.6%, and 0.9% by weight of asphalt cement. The experiment investigated the physical properties (penetration, softening point, ductility, viscosity, and specific gravity), the rheological properties (the performance grading (PG), multi-stress creep recovery (MSCR), and linear amplitude sweep (LAS)), and the microstructure and chemical composition of the modified asphalt binder. The results demonstrated impressive improvements in rutting resistance and stiffness. Adding 3% SBS and 0.9% PPA increased the rutting factor (G*/sin δ) by 165% and the high-temperature PG from 74.2 °C to 93.6 °C compared to the virgin asphalt binder. However, the optimum fatigue resistance was obtained by adding 0.3% PPA to the SBS asphalt binder. The microstructure and composition analysis revealed that using SBS and PPA together enhanced binder homogeneity and reduced voids. Lastly, an Overall Desirability (OD) analysis suggested the 3% SBS and 0.3% PPA to be the most effectively balanced formulation for the demand of high temperature and heavy traffic conditions. However, further field studies are recommended to validate the results under real-world conditions. Full article
(This article belongs to the Special Issue Advanced Asphalt Composite Materials)
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<p>Physical appearance of SBS and PPA.</p>
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<p>Binder blend preparation using a high-speed shear mixer.</p>
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<p>Overview of the experimental program.</p>
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<p>DSR-type SmartPave 102 e and testing specimens.</p>
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<p>MSCR test loading scheme and typical output strain.</p>
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<p>Instruments for microstructure and composition analysis.</p>
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<p>Variations in penetration results.</p>
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<p>Variations in softening point results.</p>
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<p>Variations in ductility results.</p>
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<p>Variations in viscosity results.</p>
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<p>Variations in specific gravity results.</p>
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<p>Variations in the rheological properties G* and δ with temperature.</p>
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<p>G*/sin δ variations with temperature and true fail temperatures.</p>
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<p>Accumulated strain vs. time curves for different asphalt binders.</p>
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<p>Effective stress vs. effective strain relationship for varying asphalt types.</p>
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<p>Fatigue life for varying binder types.</p>
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<p>FTIR results for studied binders.</p>
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<p>SEM images of: (<b>a</b>) AV, (<b>b</b>) 3% SBS, (<b>c</b>) 3% SBS + 0.3% PPA, (<b>d</b>) 3% SBS + 0.6% PPA, and (<b>e</b>) 3% SBS + 0.9% PPA.</p>
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12 pages, 4013 KiB  
Article
Effect of Turmeric Staining and Bleaching Treatment on Color Stability and Surface Hardness of Different Dental Composite Resins
by Mitsu Patel, Jimin Lee, Marc Hayashi, Reuben H. Kim and Mijoo Kim
J. Compos. Sci. 2025, 9(2), 77; https://doi.org/10.3390/jcs9020077 - 8 Feb 2025
Abstract
This study investigated the susceptibility of nine composite resins to turmeric staining, evaluated bleaching efficacy for color recovery, and assessed surface hardness throughout these processes. Disc-shaped specimens (8 mm × 2 mm, n = 3/group) were subjected to daily 20 min turmeric solution [...] Read more.
This study investigated the susceptibility of nine composite resins to turmeric staining, evaluated bleaching efficacy for color recovery, and assessed surface hardness throughout these processes. Disc-shaped specimens (8 mm × 2 mm, n = 3/group) were subjected to daily 20 min turmeric solution immersion for two weeks, followed by two weeks of daily 3 h applications of 16% carbamide peroxide bleaching. Color measurements included spectrophotometric analysis for ΔE values (threshold ΔE > 3.3 for clinical significance) and VITA Classic shade assessment at baseline, post-staining, and post-bleaching intervals. Surface hardness was evaluated using a Vickers hardness tester. Results showed significant color changes in all materials except HA after turmeric exposure, with FS exhibiting the highest staining susceptibility (ΔE = 24.6 ± 2.69) and HA showing minimal change (ΔE = 1.9 ± 0.85). VITA Classic shade evaluation revealed varying patterns; some materials maintained their initial shade designation despite significant ΔE changes (FS, CM), while others showed substantial shade shifts with successful recovery post-bleaching (HA, OM). Bleaching effectiveness varied across materials, with PO, VEP, and FS demonstrating substantial recovery in ΔE values, although FS retained clinically noticeable discoloration post-bleaching (ΔE = 7.6 ± 0.89). Surface hardness analysis revealed three distinct groups: high (80–90 HV: FS, CA, VPO), intermediate (55–70 HV: VEP, OM), and low (40–47 HV: PO, AE, HA, CM). For patients with high exposure to chromogenic foods, such as turmeric, material selection requires careful consideration of staining susceptibility, with HA and OM demonstrating superior color stability and recovery characteristics in this study. Full article
(This article belongs to the Section Composites Applications)
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<p>Color appearance of multi-shade and universal-shade composite resins at the initial phase, after turmeric staining, and after bleaching treatment.</p>
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<p>Color changes (ΔE) of composite resins. (<b>A</b>) Initial phase to staining phase, (<b>B</b>) staining phase to bleaching phase, (<b>C</b>) initial phase to bleaching phase. Different letters indicate significant differences among groups (<span class="html-italic">p</span> &lt; 0.05). Box plots show the data distribution, where “x” marks the mean, horizontal lines indicate the median, and box boundaries represent first (Q1) and third (Q3) quartiles.</p>
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<p>Vickers hardness evaluation after staining and bleaching processes. (<b>A</b>–<b>I</b>) Indentation images of FS, VEP, PO, AE, HA, CM, CA, VPO, and OM specimens. (<b>J</b>) Vickers hardness values. Different letters indicate significant differences among groups (<span class="html-italic">p</span> &lt; 0.05). Box plots show the data distribution, where “x” marks the mean, horizontal lines indicate the median, and box boundaries represent first (Q1) and third (Q3) quartiles.</p>
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12 pages, 6745 KiB  
Article
Influence of Heat Treatment on Microstructure and Wear Properties of TiC/FC250 Composites
by Yujin Lim, Jaeseong Choi, Seungchan Cho, Junghwan Kim, Sangmin Shin and Ilguk Jo
J. Compos. Sci. 2025, 9(2), 76; https://doi.org/10.3390/jcs9020076 - 8 Feb 2025
Abstract
Metal matrix composites (MMCs) produced through the unique liquid pressing infiltration (LPI) process exhibit significant industrial potential. In this study, TiC/FC250 metal matrix composites were fabricated using the liquid pressing infiltration process, and the effects of austempering and quenching–tempering heat treatments on the [...] Read more.
Metal matrix composites (MMCs) produced through the unique liquid pressing infiltration (LPI) process exhibit significant industrial potential. In this study, TiC/FC250 metal matrix composites were fabricated using the liquid pressing infiltration process, and the effects of austempering and quenching–tempering heat treatments on the microstructure and wear characteristics were investigated in comparison to as-cast specimens of both the FC250 gray cast iron matrix material and the TiC/FC250 metal matrix composites without heat treatment. The results indicated that the quenching–tempering heat treatment effectively enhanced the dry sliding friction and wear characteristics compared to the as-cast condition. The heat-treated specimens, under optimal conditions, demonstrated superior properties compared to other heat treatments and the matrix material. Although the metal matrix composites were successfully produced via the liquid pressing infiltration process and optimal heat treatment, some graphite morphology transformed from a flake to a spherical shape due to the high temperature and slow cooling rate during the process. With the quenching–tempering heat treatment, the wear resistance increased by approximately 41.53% in the matrix material and by 53.38% in the metal matrix composites compared to the as-cast specimens. The TiC/FC250 metal matrix composite heat-treated under optimal conditions exhibited an approximate 58.28% reduction in the friction coefficient compared to the FC250 gray cast iron. Full article
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<p>XRD pattern of FC250 matrix and TFC composites with different heat treatments.</p>
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<p>Scanning electron microscopy images of (<b>a</b>–<b>c</b>) FC matrix, and (<b>d</b>–<b>f</b>) TFC composites with different heat treatment. The white arrow indicates graphite.</p>
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<p>EPMA mapping analysis of specimens before heat treatment: (<b>a</b>) FC-AS (<b>b</b>) TFC-AS. The white arrow represents graphite.</p>
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<p>Hardness variation of FC and TFC metal matrix composites under different heat treatment conditions.</p>
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<p>Wear surface microscopy on the wear tracks of (<b>a</b>–<b>c</b>) FC, and (<b>d</b>–<b>f</b>) TFC metal matrix composites before and after heat treatment.</p>
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<p>High-magnification SEM images of the wear tracks of (<b>a</b>–<b>c</b>) FC250 matrix, and (<b>d</b>–<b>f</b>) TFC metal matrix composites with different heat treatment conditions. The red circle indicates the area where debris has broken off.</p>
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<p>Average friction coefficient of FC250 matrix and TFC composites with different heat treatment.</p>
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17 pages, 4583 KiB  
Article
Numerical Analysis and Life Cycle Assessment of Type V Hydrogen Pressure Vessels
by Mohd Shahneel Saharudin, Syafawati Hasbi, Santosh Kumar Sahu, Quanjin Ma and Muhammad Younas
J. Compos. Sci. 2025, 9(2), 75; https://doi.org/10.3390/jcs9020075 - 7 Feb 2025
Abstract
The growing concern about greenhouse gas emissions and global warming has heightened the focus on sustainability across industrial sectors. As a result, hydrogen energy has emerged as a versatile and promising solution for various engineering applications. Among its storage options, Type V composite [...] Read more.
The growing concern about greenhouse gas emissions and global warming has heightened the focus on sustainability across industrial sectors. As a result, hydrogen energy has emerged as a versatile and promising solution for various engineering applications. Among its storage options, Type V composite pressure vessels are particularly attractive because they eliminate the need for a polymer liner during manufacturing, significantly reducing material usage and enhancing their environmental benefit. However, limited research has explored the pressure performance and life cycle assessment of these vessels. To address this gap, this study investigates the pressure performance and carbon emissions of a Type V hydrogen pressure vessel using four composite materials: Kevlar/Epoxy, Basalt/Epoxy, E-Glass/Epoxy, and Carbon T-700/Epoxy. The results reveal that Carbon T-700/Epoxy is the most suitable material for high-pressure hydrogen storage due to its superior mechanical properties, including the highest burst pressure, maximum stress capacity, and minimal deformation under loading. Conversely, the LCA results, supported by insights from a large language model (LLM), show that Basalt/Epoxy provides a more sustainable option, exhibiting notably lower global warming potential (GWP) and acidification potential (AP). These findings highlight the trade-offs between mechanical performance and environmental impact, offering valuable insights for sustainable hydrogen storage design. Full article
(This article belongs to the Special Issue Theoretical and Computational Investigation on Composite Materials)
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<p>Geometry (<b>a</b>) and the isometric view (<b>b</b>) of the pressure vessel used in this study.</p>
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<p>Mesh dependency study.</p>
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<p>Boundary conditions on the pressure vessel.</p>
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<p>The comparison of deformation between the theoretical calculations and simulation results reveals minimal differences, indicating strong agreement between the two approaches.</p>
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<p>Top view of the hydrogen pressure vessel (no wireframe). The colour scale represents the stress distribution, where red indicates the maximum stress and blue represents the minimum stress, with a gradient transition through yellow and green.</p>
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<p>Sectional plane view of the Carbon T-700/Epoxy hydrogen pressure vessel. The colour scale represents the stress distribution, where red indicates the maximum stress and blue represents the minimum stress, with a gradient transition through yellow and green.</p>
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<p>Stacking sequence of the composites used in this study. The arrow shows the sequence in which the composite plies are stacked, moving from bottom to top.</p>
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<p>Flow chart of LLM to evaluate the environmental impact in this study.</p>
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<p>Comparison of burst pressure and allowable working pressure for different material types.</p>
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<p>Maximum principal stress vs. pressure for different materials.</p>
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<p>Maximum equivalent stress vs. pressure for different materials.</p>
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<p>Equivalent elastic strain vs. pressure for different materials.</p>
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<p>Maximum principal elastic strain vs. pressure for different materials.</p>
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<p>Global warming potential based on fibre production, resin production, aluminium boss, polyethylene coating, manufacturing, and transportation.</p>
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<p>Acidification potential from fibre production, resin curing, aluminium, and transportation.</p>
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<p>Photochemical ozone creation potential (POCP) from epoxy curing (VOCs) and NOₓ from transportation.</p>
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<p>Particulate matter formation.</p>
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23 pages, 7096 KiB  
Article
Establishing Benchmark Properties for 3D-Printed Concrete: A Study of Printability, Strength, and Durability
by Alise Sapata, Māris Šinka, Genādijs Šahmenko, Lidija Korat Bensa, Lucija Hanžič, Katarina Šter, Sandris Ručevskis, Diāna Bajāre and Freek P. Bos
J. Compos. Sci. 2025, 9(2), 74; https://doi.org/10.3390/jcs9020074 - 7 Feb 2025
Abstract
This study investigates the fresh state and hardened state mechanical and durability properties of 3D-printed concrete. The mechanical tests focused on its anisotropic behavior in response to different load orientations. Compressive, flexural, and splitting tensile strengths were evaluated relative to the print layers [...] Read more.
This study investigates the fresh state and hardened state mechanical and durability properties of 3D-printed concrete. The mechanical tests focused on its anisotropic behavior in response to different load orientations. Compressive, flexural, and splitting tensile strengths were evaluated relative to the print layers orientation. Results showed that compressive strength varied significantly, achieving 85% of cast sample strength when the load was applied parallel to the print layers ([u] direction), 71% when the load was applied perpendicular to the print object’s side plane ([v] direction), while only reaching 59% when applied perpendicular to the top plane ([w] direction). Similar trends were observed for flexural strength, with average values reaching 75% of cast sample strength when the load was applied perpendicular to the print layers ([v.u] and [w.u] directions), but decreasing to 53% when the load was applied parallel to print layers ([u.w] direction), underscoring the weaknesses at interlayer interfaces. The splitting tensile strength remained relatively consistent across print orientations, reaching 90% of the cast sample strength. Durability assessment tests revealed that 3D-printed concrete exhibits reduced resistance to environmental factors, particularly at the layer interfaces where the cold joint was formed, which are prone to moisture penetration and crack formation. These findings contribute valuable insights into the mechanical and durability properties of 3D-printed concrete, emphasizing the importance of print orientation and interlayer bonding in its performance. This understanding helps guide the optimal use of 3D-printed elements in real-life applications by aligning load or exposure to environmental factors with the material’s strength and durability characteristics. Full article
(This article belongs to the Special Issue Sustainable Composite Construction Materials, Volume II)
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<p>Custom-made laboratory concrete printer at RTU: (<b>a</b>) printer setup with the aluminum frame and print area; (<b>b</b>) gantry system closeup: (1) motor; (2) hopper; (3) inlet; (4) pipe; (5) nozzle.</p>
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<p>(<b>a</b>) Rheometer working protocol. The protocol consists of two parts with varying resting intervals: an initial resting phase of 6 min, followed by 1 min working time. After 25 min, the resting time extends to 11 min, followed by 1 min working time. (<b>b</b>) Rheological chart: time vs. torque.</p>
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<p>Specimen preparation for mechanical tests: (<b>a</b>) print object geometry for mechanical tests; (<b>b</b>) markings on specimens before cutting; (<b>c</b>) circular saw table: (1) circular saw blade; (2) metal guide fixed perpendicular to the saw blade; (3) metal guide fixed parallel to the saw blade.</p>
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<p>Test setups for compressive strength tests in various directions: (<b>a</b>) direction [u]; (<b>b</b>) direction [v]; (<b>c</b>) direction [w].</p>
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<p>Test setups for splitting strength tests in various directions: (<b>a</b>) direction [w/u]; (<b>b</b>) direction [v/w]; (<b>c</b>) direction [u/v].</p>
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<p>Test setups for flexural strength tests in various directions: (<b>a</b>) direction [u.w]; (<b>b</b>) direction [v.u]; (<b>c</b>) direction [w.u].</p>
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<p>Print object geometry for durability tests. Two printed objects: the bottom part was printed first for the object with the cold joint (T<sub>SET</sub>); the printed object without the cold joint (T<sub>0</sub>).</p>
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<p>Static and dynamic yield stress values obtained via rheometer and slugs tests.</p>
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<p>Direct buildability test: (<b>a</b>) mixture right before plastic collapse; (<b>b</b>) plastic collapse.</p>
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<p>Compressive strength test results.</p>
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<p>Comparison between compressive strength results of samples taken from different locations.</p>
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<p>Flexural strength test results.</p>
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<p>The fracture pattern of flexural strength test specimens: (<b>a</b>) direction [u.w]; (<b>b</b>) direction [v.u]; (<b>c</b>) direction [w.u].</p>
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<p>Splitting strength test results.</p>
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<p>Water absorption test results.</p>
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<p>Carbonation depth of the developed mixture after 7, 28, 56, and 90 days for (<b>a</b>) cast samples; (<b>b</b>) printed samples without the cold joint (T<sub>0</sub>); (<b>c</b>) printed samples with the cold joint (T<sub>SET</sub>).</p>
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<p>3D-printed carbonation samples after testing: (<b>a</b>) T<sub>0</sub> after 7 days; (<b>b</b>) T<sub>0</sub> after 28 days; (<b>c</b>) T<sub>0</sub> after 56 days; (<b>d</b>) T<sub>0</sub> after 90 days; (<b>e</b>) T<sub>SET</sub> after 7 days; (<b>f</b>) T<sub>SET</sub> after 28 days; (<b>g</b>) T<sub>SET</sub> after 56 days; (<b>h</b>) T<sub>SET</sub> after 90 days.</p>
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17 pages, 2785 KiB  
Article
Zn-Ferrite and Hematite Dispersed by SBA-15 Silica Grains: Visible Light-Driven Photocatalytic Activity for Advanced Oxidation Process on Amoxicillin
by Aya Jezzini, Anne Davidson, Gilles Wallez, Jean-Marc Grenèche, Tayssir Hamieh and Joumana Toufaily
J. Compos. Sci. 2025, 9(2), 73; https://doi.org/10.3390/jcs9020073 - 5 Feb 2025
Abstract
Nanoparticles of ZnFe2O4 and hematite with varied sizes and distributions were synthesized using the two-solvent method (cyclohexane, water) on SBA-15 silica batches. Calcination is performed in air at 700 °C (2 °C/min) with rapid quenching produced catalysts with distinct nanoparticle [...] Read more.
Nanoparticles of ZnFe2O4 and hematite with varied sizes and distributions were synthesized using the two-solvent method (cyclohexane, water) on SBA-15 silica batches. Calcination is performed in air at 700 °C (2 °C/min) with rapid quenching produced catalysts with distinct nanoparticle configurations, namely, internal zinc ferrite and external hematite. The choice of precursor was critical, and nitrate salts yielded only zinc ferrite nanoparticles, while chloride salts produced a mixture of hematite and zinc ferrite. The photocatalytic activity of these materials was evaluated under visible light irradiation from an LED lamp, using O2 from air as an oxidizing agent without the addition of H2O2. Samples enriched with external hematite nanoparticles from chloride precursors achieved the highest activity, decomposing 30% of AMX in 225 min. In contrast, nitrate-derived samples with predominantly internal zinc ferrite nanoparticles exhibited lower catalytic activity. Characterization via TEM, XRD, N2 sorption, and Mössbauer spectroscopy confirmed the structural and magnetic properties of the nanoparticles. Mössbauer spectra, particularly at 12K and under a magnetic field, demonstrated the presence of hematite nanoparticles, distinguishing them from isolated Fe (III) cations. Zinc ferrite nanoparticles exhibited specific magnetic ordering, with Fe ions occupying tetrahedral and octahedral sites. The results demonstrate the critical role of nanoparticle, composition, and positioning in optimizing photocatalytic efficiency for water decomposition. Full article
(This article belongs to the Section Composites Manufacturing and Processing)
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<p>N<sub>2</sub> sorption isotherms before and after impregnation: (a) SBA-15 silica alone; (b) 2S (1) nitrate; (c) 2S (2) nitrate; (d) 2S (3) nitrate impregnated.</p>
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<p>N<sub>2</sub> sorption isotherms before and after impregnation: (a) SBA-15’ alone; (b) 2S (1) chloride; (c) 2S (2) chloride, two impregnations; (d) 2S (3) chloride.</p>
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<p>XRD diffraction patterns were recorded with a diffractometer equipped with Cu Kα radiation of 2S chloride impregnated (<b>a</b>) 2S (1) chloride; (<b>b</b>) 2S (2) chloride; (<b>c</b>) 2S (3) chloride. Main crystalline phase (indexation in black): spinel ZnFe<sub>2</sub>O<sub>4</sub>. (Indexation in red): hematite.</p>
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<p>XRD diffraction patterns were recorded with a diffractometer equipped with Cu Kα radiation of 2S Nitrate impregnated (<b>a</b>) 2S (1) Nitrate; (<b>b</b>) 2S (2) Nitrate. Main crystalline phase (indexation in black): spinel ZnFe<sub>2</sub>O<sub>4</sub>.</p>
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<p>XRD diffraction patterns were recorded with a diffractometer equipped with Cu Kα radiation of: 2S Nitrate impregnated 2S (3) modeled with the Fullprof program. In red observed intensities, in black calculated intensities, in blue difference between measured and calculated intensities, and in green exact positions of the Bragg peaks.</p>
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<p>SEM micrographs of sample (<b>a</b>) 2S (1) nitrate; (<b>b</b>) SEM micrographs of sample 2S (1) chloride; (<b>c</b>) TEM micrographs of sample 2S (1) nitrate; (<b>d</b>–<b>f</b>) TEM micrographs of 2S (1) chloride.</p>
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<p>Mössbauer spectra obtained at 300 and 77 K for sample 2 S (3) and at 12 K in presence of an external magnetic field of 8T applied parallel to the γ-beam. The blue, green and red line corresponds to the ZnFe<sub>2</sub>O<sub>4</sub> phase, poorly crystallized particles and highly crystallized particles of hematite, respectively.</p>
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<p>Mössbauer spectra obtained at 300 and 77 K for sample 2 S (3) nitrate and at 12 K in presence of an external magnetic field of 8T applied parallel to the γ-beam for samples 2 S (3) nitrate and 2 S (3) nitrate after removing SBA-15 (bottom spectrum). The blue and red line corresponds to the tetrahedral and octahedral Fe sites while the green line corresponds to ultrafine NPs of ZnFe<sub>2</sub>O<sub>4</sub>.</p>
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<p>(<b>A</b>) Evolution of AMX concentration for photocatalytic tests in the presence of (a) 2S (1); (b) 2S (2); (c) 2S (3) nitrate (all samples are calcined). The concentration incertitude was between 0.02 and 0.04 mg/mL. (<b>B</b>) Evolution of AMX concentration for photocatalytic tests in the presence of (a) 2S (1), (b) 2S (2), (c) 2S (3) chloride samples (all samples are calcined). The concentration incertitude was between 0.02 and 0.04 mg/mL.</p>
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<p>Control in the dark for the third impregnation (Metallic Chloride Precursors). The concentration uncertainty was comprised between 0.02 and 0.04 mg/mL.</p>
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20 pages, 2521 KiB  
Article
A Bayesian Network Framework to Predict Compressive Strength of Recycled Aggregate Concrete
by Tien-Dung Nguyen, Rachid Cherif, Pierre-Yves Mahieux and Emilio Bastidas-Arteaga
J. Compos. Sci. 2025, 9(2), 72; https://doi.org/10.3390/jcs9020072 - 5 Feb 2025
Abstract
In recent years, the use of recycled aggregate concrete (RAC) has become a major concern when promoting sustainable development in construction. However, the design of concrete mixes and the prediction of their compressive strength becomes difficult due to the heterogeneity of recycled aggregates [...] Read more.
In recent years, the use of recycled aggregate concrete (RAC) has become a major concern when promoting sustainable development in construction. However, the design of concrete mixes and the prediction of their compressive strength becomes difficult due to the heterogeneity of recycled aggregates (RA). Artificial-intelligence (AI) approaches for the prediction of RAC compressive strength (fc) need a sizable database to have the ability to generalize models. Additionally, not all AI methods may update input values in the model to improve the performance of the algorithms or to identify some model parameters. To overcome these challenges, this study proposes a new method based on Bayesian Networks (BNs) to predict the fc of RAC, as well as to identify some parameters of the RAC formulation to achieve a given fc target. The BN approach utilizes the available data from three input variables: water-to-cement ratio, aggregate-to-cement ratio, and RA replacement ratio to calculate the prior and posterior probability of fc. The outcomes demonstrate how BNs may be used to forecast both forward and backward, related to the fc of RAC, and the parameters of the concrete formulation. Full article
(This article belongs to the Special Issue Novel Cement and Concrete Materials)
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<p>A schematic BN.</p>
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<p>Objectives of the two considered case studies: (<b>a</b>) prediction of <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>f</mi> </mrow> <mrow> <mi>c</mi> </mrow> </msub> </mrow> </semantics></math>, (<b>b</b>) formulation design for a target <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>f</mi> </mrow> <mrow> <mi>c</mi> </mrow> </msub> </mrow> </semantics></math>.</p>
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<p>Proposed BNs model.</p>
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<p>Scatterplot for the database.</p>
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<p>Correlation matrix of input parameters.</p>
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<p>Prior probability of all nodes.</p>
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<p>Posterior probability of compressive strength.</p>
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<p>Posterior probabilities of <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>f</mi> </mrow> <mrow> <mi>c</mi> </mrow> </msub> </mrow> </semantics></math> node for several pieces of evidence.</p>
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<p>Means for <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>f</mi> </mrow> <mrow> <mi>c</mi> </mrow> </msub> </mrow> </semantics></math> obtained with BNs and experimental data.</p>
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<p>Prior distributions of the parent nodes and evidence of the child node.</p>
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<p>Posterior probabilities of the parent nodes.</p>
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28 pages, 2319 KiB  
Review
Advancements in Free-Standing Ferroelectric Films: Paving the Way for Transparent Flexible Electronics
by Riya Pathak, Gopinathan Anoop and Shibnath Samanta
J. Compos. Sci. 2025, 9(2), 71; https://doi.org/10.3390/jcs9020071 - 5 Feb 2025
Abstract
Free-standing ferroelectric films have emerged as a transformative technology in the field of flexible electronics, offering unique properties that enable a wide range of applications, including sensors, actuators, and energy harvesting devices. This review paper explores recent advancements in the fabrication, characterization, and [...] Read more.
Free-standing ferroelectric films have emerged as a transformative technology in the field of flexible electronics, offering unique properties that enable a wide range of applications, including sensors, actuators, and energy harvesting devices. This review paper explores recent advancements in the fabrication, characterization, and application of free-standing ferroelectric films, highlighting innovative techniques such as multilayer structures and van der Waals epitaxy that enhance their performance while maintaining mechanical flexibility. We discuss the critical role of these films in next-generation devices, emphasizing their potential for integration into multifunctional systems that combine energy harvesting and sensing capabilities. Additionally, we address challenges related to leakage currents, polarization stability, and scalability that must be overcome to facilitate commercialization. By synthesizing current research findings and identifying future directions, this paper aims to provide a comprehensive overview of the state-of-the-art in free-standing ferroelectric films and their impact on the development of sustainable and efficient flexible electronic technologies. Full article
(This article belongs to the Section Composites Applications)
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<p>A schematic diagram illustrating the laser lift-off process. This figure is intended to provide a general overview of the methodology and does not depict specific experimental parameters.</p>
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<p>A schematic representation of the wet etching process for fabricating free-standing ferroelectric films.</p>
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<p>Interfaces connected by Van der Waals gap.</p>
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<p>Comparison of remnant polarization (P<sub>r</sub>) of substrate intact and free-standing ferroelectric films.</p>
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<p>Roadmap of domain wall motion in free-standing films. The orange color represents the ferroelectric film.</p>
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<p>(<b>a</b>–<b>c</b>): Schematic illustration of an energy harvesting mechanism where bending the substrate induces mechanical strain in the ferroelectric layer, leading to the switching of polarization domains. Arrows indicate the direction of polarization of each domain.</p>
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<p>Integration of free-standing films in multifunctional devices.</p>
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15 pages, 2601 KiB  
Article
Physicochemical Studies of Opoka as a Raw Material Component of Sodium Silicate Mixture for Subsequent Synthesis of Foam Glass Material Based on It
by Bibol Zhakipbayev, Alexandr Kolesnikov, Samal Syrlybekkyzy, Leila Seidaliyeva, Akmaral Koishina and Lyailim Taizhanova
J. Compos. Sci. 2025, 9(2), 70; https://doi.org/10.3390/jcs9020070 - 4 Feb 2025
Abstract
The present article presents the results of physical and chemical studies of opoka. In particular, the opoka was subjected to chemical analysis, X-ray phase, differential thermal analysis, scanning microscopy, and X-ray energy dispersive elemental microanalysis. The opoka was studied with the aim of [...] Read more.
The present article presents the results of physical and chemical studies of opoka. In particular, the opoka was subjected to chemical analysis, X-ray phase, differential thermal analysis, scanning microscopy, and X-ray energy dispersive elemental microanalysis. The opoka was studied with the aim of using it as an available raw material for obtaining a sodium silicate mixture and, in the future, developing an energy-saving technology for obtaining a building heat-insulating and sound-insulating foam glass material based on it, using synthesis. As a result of the studies, the chemical composition of the opoka was determined, which is 69–80% represented by silica. The elemental composition of the opoka was established, which is represented by 94.25% oxides of Si, Al, and Fe. The presence of such oxides makes it an ideal raw material component of a silicate-sodium mixture for the subsequent synthesis of foam glass material from it. Experimental exploratory studies on the synthesis of foam glass based on opoka have been carried out. The experimentally obtained sample of foam glass material consists of 93.37% Si, Al, Mg, and Na oxides, has a porous structure with a pore size of 2–5 microns, an average density of 375 kg/m3, thermal conductivity of 0.063 W/(m °C) at 25 °C, and noise absorption of 51.6 Db. Full article
(This article belongs to the Section Composites Manufacturing and Processing)
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<p>Differential thermal analysis of the selected sample of opoka from the Orangay deposit.</p>
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<p>Microphotographs of the structure of opoka from the Orangay deposit obtained on a scanning electron microscope at different magnifications: (<b>a</b>) 250; (<b>b</b>) 500; (<b>c</b>) 1000; (<b>d</b>) 2000 times.</p>
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<p>Microphotographs of the structure of opoka from the Orangay deposit obtained on a scanning electron microscope at different magnifications: (<b>a</b>) 250; (<b>b</b>) 500; (<b>c</b>) 1000; (<b>d</b>) 2000 times.</p>
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<p>Electron microscopic analysis of a selected opoka sample from the Orangay deposit obtained using a scanning electron microscope: (<b>a</b>) micrography; (<b>b</b>) elemental chemical analysis.</p>
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<p>Electron microscopic analysis of an optimal foam glass sample based on opoka obtained as a result of experimental exploratory synthesis: (<b>a</b>) micrography; (<b>b</b>) elemental chemical analysis.</p>
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15 pages, 4027 KiB  
Article
Thermal, Mechanical, and Microstructural Properties of Novel Light Expanded Clay Aggregate (LECA)-Based Geopolymer Concretes
by Tinkara Marija Podnar and Gregor Kravanja
J. Compos. Sci. 2025, 9(2), 69; https://doi.org/10.3390/jcs9020069 - 4 Feb 2025
Abstract
The construction sector’s reliance on traditional cement significantly contributes to CO2 emissions, underscoring the urgent need for sustainable alternatives. This study investigates fine (0–4 mm), rounded, uncoated, porous-surfaced lightweight expanded clay aggregate (LECA)-based geopolymers, which combine the low-carbon benefits of geopolymers with [...] Read more.
The construction sector’s reliance on traditional cement significantly contributes to CO2 emissions, underscoring the urgent need for sustainable alternatives. This study investigates fine (0–4 mm), rounded, uncoated, porous-surfaced lightweight expanded clay aggregate (LECA)-based geopolymers, which combine the low-carbon benefits of geopolymers with LECA’s lightweight and insulating properties. Geopolymers were synthesized using lignite-rich fly ash with varying ratios of LECA to aggregate. Mechanical testing revealed that the reference mixture without LECA (REF-GEO) achieved the highest compressive strength of 37.89 ± 0.75 MPa and flexural strength of 7.62 ± 0.11 MPa, while complete substitution of the aggregate with LECA (LECA-100%) reduced the compressive strength to 17.31 ± 0.88 MPa and flexural strength to 3.41 ± 0.11 MPa. The density of the samples decreased from 2.06 g/cm3 for REF-GEO to 1.31 g/cm3 for LECA-100%, and thermal conductivity dropped significantly from 1.15 ± 0.07 W/mK to 0.38 ± 0.01 W/mK. Microstructural analysis using XRD and SEM-EDX highlighted changes in the material’s internal structure and the increase in porosity with higher LECA content. Water vapor permeability increases over time, particularly in samples with higher LECA content. These findings suggest that LECA-based geopolymers are suitable for low-load or non-structural elements. They are ideal for sustainable, energy-efficient construction that requires lightweight, insulating, and breathable materials. Full article
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<p>(<b>a</b>) Granulometric analysis for lignite-based fly ash and (<b>b</b>) example of dynamic image analysis.</p>
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<p>(<b>a</b>) The fractured REF-GEO sample, showing visible aggregates (<b>b</b>), and the 100% LECA sample, with dark spots indicating LECA inclusions within the matrix at the cross-section.</p>
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<p>Schematic representation of the method.</p>
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<p>(<b>a</b>) Compressive and (<b>b</b>) flexural strength data.</p>
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<p>(<b>a</b>) Density and (<b>b</b>) thermal conductivity at 28 days.</p>
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<p>XRD of LECA grains.</p>
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<p>SEM micrographs of LECA grains.</p>
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<p>SEM micrographs of the REF-GEO sample.</p>
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<p>SEM micrographs of the LECA-100% sample.</p>
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<p>SEM-EDX and elemental composition analysis for the LECA-100% sample.</p>
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<p>Transmitted water vapor measurements.</p>
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12 pages, 970 KiB  
Article
Enhanced Photocatalytic Hydrogen Generation from Methanol Solutions via In Situ Ni/Pt Co-Deposition on TiO2
by Mst. Farhana Afrin, Mai Furukawa, Ikki Tateishi, Hideyuki Katsumata, Monir Uzzaman and Satoshi Kaneco
J. Compos. Sci. 2025, 9(2), 68; https://doi.org/10.3390/jcs9020068 - 2 Feb 2025
Abstract
TiO2 is widely utilized as an excellent photocatalyst in energy production. However, its rapid electron and hole recombination confers poor photocatalytic activity. Cocatalysts are essential for increasing photocatalytic efficacy by introducing improved electron transmission and enlarging the active site. Herein, the photocatalytic [...] Read more.
TiO2 is widely utilized as an excellent photocatalyst in energy production. However, its rapid electron and hole recombination confers poor photocatalytic activity. Cocatalysts are essential for increasing photocatalytic efficacy by introducing improved electron transmission and enlarging the active site. Herein, the photocatalytic degradation of aqueous methanol solution to generate hydrogen was studied with the simultaneous in situ deposition of metals (M = Ag, Cu, Ni, Pd, and Pt) on the TiO2 surface. Adding methanol to water and incorporating a bimetallic cocatalyst enhanced hydrogen production by reducing the electron–hole pair recombination. The studied metal ions could be reduced by the conduction band electrons of TiO2 for the in situ simultaneous deposition of metal. The larger work function value of the studied metals favored the Schottky junction formation, which contributed to increasing photocatalytic efficiency. Among these simultaneous metal-deposited photocatalysts, maximal photocatalytic hydrogen production was achieved with NiPt/TiO2. The optimal component was 0.01 wt.% Ni/1.0 wt.% Pt for TiO2. The hydrogen evolution with NiPt/TiO2 was approximately 341 and 1.3 times better than that with pure TiO2 and Pt/TiO2, respectively. A potential reaction pathway for photocatalytic hydrogen production from an aqueous methanol solution over NiPt/TiO2 photocatalyst has also been proposed. Full article
(This article belongs to the Special Issue Feature Papers in Journal of Composites Science in 2024)
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<p>Effect of in situ simultaneous deposition of (<b>a</b>) Pt and (<b>b</b>) Ag on TiO<sub>2</sub> for hydrogen production from aqueous methanol solution.</p>
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<p>Effect of in situ simultaneous Pt and Cu deposition on photocatalytic hydrogen production with TiO<sub>2</sub> from aqueous methanol solution for 3 h.</p>
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<p>Effect of in situ simultaneous Pt and Ni deposition on photocatalytic hydrogen production with TiO<sub>2</sub> from aqueous methanol solution for 3 h.</p>
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<p>Reaction mechanism of photocatalytic hydrogen production from the aqueous methanol solution using the TiO<sub>2</sub> photocatalyst with the simultaneous photodeposition of Ni and Pt.</p>
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22 pages, 5276 KiB  
Article
Development of Doum Palm Fiber-Based Building Insulation Composites with Citric Acid/Glycerol Eco-Friendly Binder
by Hicham Elmoudnia, Younoussa Millogo, Paulina Faria, Rachid Jalal, Mohamed Waqif and Latifa Saâdi
J. Compos. Sci. 2025, 9(2), 67; https://doi.org/10.3390/jcs9020067 - 2 Feb 2025
Abstract
This study focuses on the development of an insulation biocomposite using Doum palm (Chamaerops humilis) fibers reinforced with a natural binder based on citric acid and glycerol. The main objective is to optimize the thermal conductivity and mechanical properties of the biocomposite as [...] Read more.
This study focuses on the development of an insulation biocomposite using Doum palm (Chamaerops humilis) fibers reinforced with a natural binder based on citric acid and glycerol. The main objective is to optimize the thermal conductivity and mechanical properties of the biocomposite as a function of fiber preparation (short or powdered fibers) and binder content (20%, 30% and 40%), and relate them to the bonding of the fibers and the binder. The obtained results suggest that the addition of the binder greatly enhances the density, compressive strength and Young’s modulus of biocomposites. More specifically, the addition of 20% by weight of the citric acid/glycerol binder improves the bond between fibers, whether they are short fibers or powders. This leads to an increase in the mechanical properties, with Young’s modulus reaching (212.1) MPa and compressive strength at (24.3) MPa. On the other hand, the results show that these biocomposites also have acceptable thermal insulation performance, achieving a thermal conductivity of (0.102) W/(m·K), making them suitable for a variety of applications in sustainable buildings and for refurbishment. Full article
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<p>Binder preparation protocol with glycerol, citric acid, water and catalyst, with thermal treatments.</p>
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<p>Preparation of the fibers: (<b>a</b>) Chamaerops humilis; (<b>b</b>) chopped fibers; (<b>c</b>) cut fibers; (<b>d</b>) mill used to prepare the fibers; (<b>e</b>) short and (<b>f</b>) powdered fibers.</p>
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<p>Composite specimens and thermal and mechanical experimental tests carried out.</p>
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<p>SEM EDX analysis of DPfs.</p>
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<p>FTIR spectra of DPfs in the raw state.</p>
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<p>X-ray diffractogram of DPfs in the raw state.</p>
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<p>ATG-ATD curves of raw DPfs.</p>
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<p>SEM observation of untreated DPfs.</p>
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<p>Infrared spectrum of the biosourced binder synthesized based on CA-GLY.</p>
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<p>Reactions involving both citric acid and glycerol molecules in condensation.</p>
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<p>Mechanical properties of DPf-based specimens at different sizes with b-average and standard deviation: (<b>a</b>): compressive strength; (<b>b</b>): Young’s modulus.</p>
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<p>Thermal conductivity of Doum fiber-based test pieces at various sizes.</p>
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22 pages, 13498 KiB  
Article
A Study on the Relationship Between the Pore Characteristics of High-Performance Self-Compacting Concrete (HPSCC) Based on Fractal Theory and the Function of the Water–Binder Ratio (W/C)
by Guihong Xu, Mingwei He, Li He, Yongsheng Chen, Li Duan and Weiguo Jiao
J. Compos. Sci. 2025, 9(2), 66; https://doi.org/10.3390/jcs9020066 - 2 Feb 2025
Abstract
The mechanical properties of High-Performance Self-Compacting Concrete (HPSCC) are strongly influenced by its pore structure, but the impact of varying water–binder ratios (W/C) on this relationship remains unclear. To address this, the present study investigates HPSCC with W/C ratios ranging from 0.19 to [...] Read more.
The mechanical properties of High-Performance Self-Compacting Concrete (HPSCC) are strongly influenced by its pore structure, but the impact of varying water–binder ratios (W/C) on this relationship remains unclear. To address this, the present study investigates HPSCC with W/C ratios ranging from 0.19 to 0.23, aiming to elucidate the connection between pore structure, fractal characteristics, and mechanical performance. Through a combination of compressive strength testing, low-temperature nitrogen adsorption, and Scanning Electron Microscopy (SEM) observations, this study reveals key insights. First, compressive strength initially increases with a decreasing W/C ratio but plateaus beyond W/C = 0.21, identifying an optimal range for balancing strength and workability. Second, the pore structure of HPSCC is characterized by cylindrical, ink-bottle, and planar interstitial pores, with significant fractal characteristics. Notably, the fractal dimension decreases as the W/C ratio increases, indicating reduced pore complexity and improved homogeneity. Finally, a strong linear correlation (R2 > 0.9) between the W/C ratio, fractal dimension, and compressive strength provides a predictive tool for assessing HPSCC performance. This study concludes that the internal pore structure is a critical determinant of HPSCC strength, and the identified optimal W/C ratio range offers guidance for mixture designs. Additionally, fractal dimension analysis emerges as a novel method to evaluate HPSCC’s microstructural quality, enabling predictions of long-term performance and durability. These findings contribute to the scientific basis for designing high-performance concrete materials with improved mechanical properties and durability. Full article
(This article belongs to the Special Issue Novel Cement and Concrete Materials)
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<p>Classification of pore types. (<a href="#jcs-09-00066-f001" class="html-fig">Figure 1</a>: The International Union of Pure and Applied Chemistry, abbreviated as “IUPAC”, is an internationally recognized standard for pore size classification proposed by the International Union of Pure and Applied Chemistry [<a href="#B6-jcs-09-00066" class="html-bibr">6</a>]. The “Hodot” classification method was a coal pore size classification scheme proposed by the Soviet scholar Khodot (Xoдoт, B.B.) in 1966 [<a href="#B6-jcs-09-00066" class="html-bibr">6</a>]).</p>
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<p>Pore structure determination method.</p>
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<p>Scored screen allowance and cumulative screen allowance of machine-made sand.</p>
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<p>Diagram of particle size cumulative distribution.</p>
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<p>Particle size distribution.</p>
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<p>HPSCC experimental samples’ preparation process.</p>
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<p>HPSCC-A adsorption/desorption isotherms. In the area of relatively low pressure (<math display="inline"><semantics> <mrow> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 0.45), the curve rises slowly, and the adsorption and desorption curves coincide, indicating that the concrete is mainly composed of cylindrical pores and wedge-shaped pores. As the relative pressure increases, when <math display="inline"><semantics> <mrow> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>≥</mo> </mrow> </semantics></math> 0.45, the adsorption–desorption curve shows a separation, forming a large hysteresis loop, indicating that within this pressure range, the adsorbate mainly exists in the form of “ink-bottle” or “impermeable” pores. At the end of the curve, the adsorption–desorption curves tend to coincide, which indicates that the internal structure of the cementitious material has a “crack-pore” or “interstices” or “slit-like” particles formed in the plate. The adsorption capacity of the sample at the maximum relative pressure area is 0.3 mL/g.</p>
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<p>HPSCC-B adsorption/desorption isotherms. In the area of <math display="inline"><semantics> <mrow> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 0.93, the curve rises slowly, and the adsorption and desorption curve are separated. This shows that the adsorbent in concrete does not completely dissociate; therefore, its pore shape is mainly “ink-bottle” and “spherical” air-tight pores. In the area of 0.93 <math display="inline"><semantics> <mrow> <mo>≤</mo> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 1, the adsorption and desorption curves tend to coincide, suggesting that the sample has a “slit-like” structure formed by cracks or “interstices” particles inside.</p>
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<p>HPSCC-C Adsorption/desorption isotherms. The adsorption-desorption isotherms are similar to <a href="#jcs-09-00066-f008" class="html-fig">Figure 8</a>. In the area of <math display="inline"><semantics> <mrow> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 0.93, the sample is mainly composed of “ink-bottle” and “spherical” air-tight pores. At a relative pressure of 0.93 <math display="inline"><semantics> <mrow> <mo>≤</mo> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 1, the sample has a “slit-like” structure formed by cracks or “interstices” particles inside.</p>
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<p>HPSCC-D adsorption/desorption isotherms. The adsorption–desorption isotherms are similar to <a href="#jcs-09-00066-f011" class="html-fig">Figure 11</a>. Therefore, the pore structure is similar to that of HPSCC-A. The maximum adsorption capacity is 0.3 mL/g.</p>
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<p>HPSCC-E adsorption/desorption isotherms. In the area of relatively low pressure (<math display="inline"><semantics> <mrow> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 0.42), the experimental results only show the adsorption curve, indicating that within this pressure range, the adsorbate did not desorb and remained completely inside the pores. As the relative pressure increases, when 0.42 <math display="inline"><semantics> <mrow> <mo>≤</mo> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 0.8, the adsorption–desorption curve shows a separation, and the adsorption pores mainly exists in the form of “ink-bottle” or “impermeable” pores. At the end of the curve (0.8 <math display="inline"><semantics> <mrow> <mo>≤</mo> <mi>P</mi> <mo>/</mo> <msub> <mi>P</mi> <mn>0</mn> </msub> <mo>&lt;</mo> </mrow> </semantics></math> 1), the adsorption–desorption curves tend to coincide, which indicates that the internal structure of the cementitious material has a “crack-pore” or “interstices” or “slit-like” particles formed in the plate.</p>
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<p>BJH (desorption) pore area and pore size curve and morphology.</p>
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<p>HPSCC-B BJH (desorption) pore area and pore size curve and Morphology.</p>
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<p>HPSCC-C BJH (desorption) pore area and pore size curve and morphology.</p>
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<p>HPSCC-D BJH (desorption) pore area and pore size curve and morphology.</p>
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<p>HPSCC-E BJH (desorption) pore area and pore size curve and morphology.</p>
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<p>Low-temperature liquid nitrogen adsorption volume fractal dimension fitting diagram of HPSCC-A. The fitting equation is K = −0.55, the correlation coefficient R<sup>2</sup> is 0.95, and the fitting curve has a good correlation with the experimental curve. The fractal dimension D is 2.45.</p>
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<p>Low-temperature liquid nitrogen adsorption volume fractal dimension fitting diagram of HPSCC-B. The fitting equation is K = −0.63. Because the experimental curve fluctuates greatly, the correlation coefficient R<sup>2</sup> is 0.88. The fitting curve deviates from the experimental curve. The correlation coefficient R is a statistical index used to reflect the close degree of correlation between variables. It is generally considered that when <math display="inline"><semantics> <mrow> <msup> <mi mathvariant="normal">R</mi> <mn>2</mn> </msup> <mo>&gt;</mo> <mn>0</mn> <mrow> <mo>.</mo> <mn>86</mn> </mrow> </mrow> </semantics></math>, the correlation between the two curves is good, and the fitting curve is acceptable. The fractal dimension D was calculated to be 2.37.</p>
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<p>Low-temperature liquid nitrogen adsorption volume fractal dimension fitting diagram of HPSCC-C. The fitting equation is <span class="html-italic">K</span> = −0.65, the correlation coefficient R<sup>2</sup> is 0.87, and the fractal dimension <span class="html-italic">D</span> is 2.35.</p>
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<p>Low-temperature liquid nitrogen adsorption volume fractal dimension fitting diagram of HPSCC-D. The fitting equation is K = −0.67, the correlation coefficient R<sup>2</sup> is 0.93, and the fitting curve has a good correlation with the experimental curve. The fractal dimension D is 2.33.</p>
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<p>Low-temperature liquid nitrogen adsorption volume fractal dimension fitting diagram of HPSCC-E. The fitting equation is K = −0.70, the correlation coefficient R<sup>2</sup> is 0.977, and the fitting curve has a good correlation with the experimental curve. The fractal dimension D is 2.30.</p>
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<p>Relation between W/C and compressive strength.</p>
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<p>Relationship between W/C and BJH average pore size.</p>
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<p>Relational curve between W/C and fractal dimension.</p>
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<p>The relational curve between compressive strength and fractal dimension.</p>
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18 pages, 5155 KiB  
Article
Antibacterial UV-Curable Gel with Hydroxyapatite Nanoparticles for Regenerative Medicine in the Field of Orthopedics
by Julia A. Burunkova, Valeria V. Semykina, Vera E. Sitnikova, Dmitry M. Dolgintsev, Faliya F. Zaripova, Alina A. Ponomareva, Diana R. Mizina, Attila Csick, Sandor Kokenyesi and Anton Zhilenkov
J. Compos. Sci. 2025, 9(2), 65; https://doi.org/10.3390/jcs9020065 - 1 Feb 2025
Abstract
The development and analysis of the properties of a new material based on UV-curable acrylate monomers with silicon-containing hydroxyapatite and zinc oxide nanoparticles as an antibacterial component and gelatin was carried out. Using this material in orthopedics and dentistry is very convenient because [...] Read more.
The development and analysis of the properties of a new material based on UV-curable acrylate monomers with silicon-containing hydroxyapatite and zinc oxide nanoparticles as an antibacterial component and gelatin was carried out. Using this material in orthopedics and dentistry is very convenient because it covers any surface geometry of metal implants and hardens under ultraviolet light. In this work, sorption properties, changes in porosity, and mechanical properties of the material were investigated. The conditions for obtaining hydroxyapatite (HA) nanoparticles and the presence of silicon oxide nanoparticles and organic for the shell in an aqueous medium were studied for the pH of the medium, the sequence of administration and concentration of the material components, as well as antibacterial properties. This polymer material is partially resorbable. That supports not only the growth of bone cells but also serves as a protective layer. It reduces friction between organic tissues and a metal implant and can be a solution to the problem of the aseptic instability of metal implants. The material can also be used to repair damaged bones and cartilage tissues, especially in cases where the application and curing procedure is performed using laparoscopic methods. In this work, the authors propose a simple and quite cheap method for obtaining material based on photopolymerizable acrylates and natural gelatin with nanoparticles of HA, zinc oxide, and silicon oxide. The method allows one to obtain a composite material with different nanoparticles in a polymer matrix which retain the requisite properties needed such as active-sized HA, antibacterial ZnO, and structure-forming and stability-improving SiO2 nanoparticles. Full article
(This article belongs to the Section Biocomposites)
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<p>The structural formula of the Bis—GMA acrylate monomer.</p>
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<p>Size of HA particles: (<b>a</b>) in the presence of carboxylate and silicon oxide nanoparticles; (<b>b</b>) in the presence of 2-carboxylate, silicon nanoparticles, and gelatin (<b>q</b> (%)—percentage of particles by diameter; undersize—total particle content).</p>
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<p>Energy-dispersive spectra of hydroxyapatite samples: (<b>a</b>) in presence of carboxylate and silicon oxide nanoparticles; (<b>b</b>) after addition of gelatin.</p>
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<p>XRD results of HA powder samples (<a href="#jcs-09-00065-t002" class="html-table">Table 2</a>) obtained in aqueous solution with different accompanying components: (<b>a</b>) HA (sample 1) and HA particles formed in the presence of silicon oxide nanoparticles only (sample 2); (<b>b</b>) HA (sample 1) and HA nanoparticles formed in solution with 2Ccarboxylate (sample 3); (<b>c</b>) HA (sample 1) and HA particles formed in the simultaneous presence of silicon oxide nanoparticles and 2Carboxylate (sample 1).</p>
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<p>IR spectra: 1—silica hydroxyapatite nanoparticles (black, sample 2 in <a href="#jcs-09-00065-t002" class="html-table">Table 2</a> or <a href="#jcs-09-00065-t003" class="html-table">Table 3</a>); 2—silica hydroxyapatite nanoparticles surface-modified with 2Carboxylate (red, sample 4 in <a href="#jcs-09-00065-t002" class="html-table">Table 2</a> or <a href="#jcs-09-00065-t003" class="html-table">Table 3</a>); 3—monomer 2Carboxylate (blue).</p>
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<p>Composite image 1. (<b>a</b>)—Optical microscope; (<b>b</b>)—TEM.</p>
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<p>Changes in relative mass of film samples (<a href="#jcs-09-00065-t001" class="html-table">Table 1</a>) when soaking in water: (<b>a</b>) nanocomposites 2 (Bis1/1 + ZnO) and 4 (Bis4/6 +ZnO) based on monomers only; (<b>b</b>) nanocomposites 1 (Bis1/1 + Gel + ZnO) and 3 (Bis4/6 + Gel + ZnO) based on monomers with gelatin.</p>
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<p>Creep curves of dry polymeric materials (<b>a</b>) and wet polymeric materials (after staying in phosphate buffer solution—PBS, wet); (<b>b</b>) at a constant stress level of 1 MPa and 37 °C (ε-creep [%]).</p>
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<p>Dry sample: Bis1/1 + Gel + ZnO, Bis4/6 + Gel + ZnO, Bis6/4 + Gel + ZnO; 1 multi-step creep response of polymer samples at 37 °C and at 30 min steps. (<b>a</b>)—Strain–relaxation cycles; (<b>b</b>)—residual strain (∆L/L<sub>0</sub>—slope of relative change in length; ε-creep [%]).</p>
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<p>Multi-step creep response of samples at 37 °C and body conditions for wet state after 14 days in PBS (phosphate buffer): (<b>a</b>)—deformation–relaxation cycles; (<b>b</b>)—accumulation of permanent deformation.</p>
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<p>Antimicrobial activity test results (on solid nutrient medium BisA-2Car/SiO2_HA/Gel with and without ZnO): (<b>a</b>) preliminary results. Sample 2 in the Petri dish has ZnO; other samples have a similar composition but are without zinc oxide. Photos of samples after 10 days: 1—<span class="html-italic">Candida albicans</span>; 3—<span class="html-italic">Staphylococcus aureus</span>; 5—<span class="html-italic">Escherichia coli</span>; 6—<span class="html-italic">Klebsiella pneumonia</span>; 7—<span class="html-italic">Acinetobacter baumannii</span>; (<b>b</b>,<b>c</b>) studies of the antimicrobial activity of the composite over time: (<b>b</b>)—<span class="html-italic">Klebsiella pneumoniae</span>; (<b>c</b>)—<span class="html-italic">Staphylococcus aureus</span>.</p>
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14 pages, 5278 KiB  
Article
Microwave Synthesis of Luminescent Recycled Glass Containing Dy2O3 and Sm2O3
by Achanai Buasri, Apichaya Boonpanya, Arraya Yangderm, Thanaporn Kensopha and Vorrada Loryuenyong
J. Compos. Sci. 2025, 9(2), 64; https://doi.org/10.3390/jcs9020064 - 1 Feb 2025
Abstract
This research studied the recycling of borosilicate glass wastes from damaged laboratory glassware. The luminescent glasses were prepared by doping glass waste powder with rare earth ions, namely, dysprosium ions (Dy3+) and samarium ions (Sm3+), as well as co-doping [...] Read more.
This research studied the recycling of borosilicate glass wastes from damaged laboratory glassware. The luminescent glasses were prepared by doping glass waste powder with rare earth ions, namely, dysprosium ions (Dy3+) and samarium ions (Sm3+), as well as co-doping with Dy3+ and Sm3+ at a concentration of 2% by weight. The sintering process was conducted in a microwave oven for a duration of 15 min. The photoluminescence spectra of the doped glasses were obtained under excitation at 401 nm and 388 nm. The results showed that the emission characteristics depended on the doping concentrations of Dy3+ and Sm3+ and the excitation wavelengths. Upon excitation at 401 nm, the co-doped glasses exhibited the maximum emission peak of Sm3+ at 601 nm (yellowish and orange region in the CIE chromaticity diagram) due to the energy transition from 4G5/2 to 6H7/2. When excited at 388 nm, however, the emission spectra of the co-doped glasses were similar to the characteristic emission peaks of Dy3+ (white region in the CIE chromaticity diagram), but the peak position exhibits a red shift. This could be attributed to an increase in the amount of non-bridging oxygens (NBOs) by co-doping. Full article
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<p>The physical and structural properties of undoped glasses sintered by (<b>a</b>) the conventional sintering method at different temperatures for 1 h and (<b>b</b>) the microwave sintering method at 800 W for different durations.</p>
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<p>Digital images of glass samples under daylight and UV irradiation.</p>
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<p>Apparent density of Dy<sup>3+</sup>- and Sm<sup>3+</sup>-doped glass samples.</p>
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<p>XRD patterns of (<b>a</b>) MD0, (<b>b</b>) MD1, (<b>c</b>) MD2, (<b>d</b>) MD3, (<b>e</b>) MD4, and (<b>f</b>) MD5.</p>
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<p>FTIR spectra of (<b>a</b>) MD0, (<b>b</b>) MD1, (<b>c</b>) MD2, (<b>d</b>) MD3, (<b>e</b>) MD4, and (<b>f</b>) MD5.</p>
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<p>Absorption spectra of (<b>a</b>) MD1, (<b>b</b>) MD2, (<b>c</b>) MD3, (<b>d</b>) MD4, and (<b>e</b>) MD5. (*—Dy<sup>3+</sup>, Δ—Sm<sup>3+</sup>).</p>
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<p>SEM images of glass samples’ fractured surfaces.</p>
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<p>(<b>a</b>) Excitation spectra monitoring at 601 nm emission wavelength and (<b>b</b>) emission spectra monitoring at 401 nm excitation wavelength of Dy<sup>3+</sup>- and Sm<sup>3+</sup>-doped glass samples.</p>
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<p>(<b>a</b>) Excitation spectra monitoring at 574 nm emission wavelength and (<b>b</b>) emission spectra monitoring at 388 nm excitation wavelength of Dy<sup>3+</sup>- and Sm<sup>3+</sup>-doped glass samples.</p>
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<p>The overlap between the emission spectrum of MD1 (Dy<sup>3+</sup>) and excitation spectra of MD5 (Sm<sup>3+</sup>).</p>
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<p>CIE 1931 Chromaticity diagram of Dy<sup>3+</sup>- and Sm<sup>3+</sup>-doped glass samples under excitation at (<b>a</b>) 401 nm and (<b>b</b>) 388 nm.</p>
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18 pages, 7322 KiB  
Article
Optimization of 3D Printing Parameters for Enhanced Mechanical Strength: Effects of Glass Fiber Reinforcement and Fill Ratio Using RSM and ANOVA
by Hussein Hadi Jawad, Naser Kordani, Abbasali Bagheri and Hamed Aghajani Derazkola
J. Compos. Sci. 2025, 9(2), 63; https://doi.org/10.3390/jcs9020063 - 1 Feb 2025
Abstract
This research aimed to provide valuable insights for future studies and enhance manufacturing processes by investigating the effect of incorporating fibers into 3D printing to improve the mechanical properties of fabricated components. The experimental design was carried out using Design-Expert software, employing the [...] Read more.
This research aimed to provide valuable insights for future studies and enhance manufacturing processes by investigating the effect of incorporating fibers into 3D printing to improve the mechanical properties of fabricated components. The experimental design was carried out using Design-Expert software, employing the Central Composite Design (CCD) methodology. Seventeen experiments were conducted, with predefined input parameters, layer height, filler ratio, and printing speed, analyzed through the Response Surface Methodology (RSM) using Design-Expert version 12. An Analysis of Variance (ANOVA) revealed that the filler ratio had the most significant effect on fracture strength. The influence of different printing parameters printing speed, layer height, and filler ratio on the mechanical properties and print quality was systematically investigated. The results indicated that the filler ratio was the most critical factor, with a 100% fill ratio yielding the highest tensile strength. Conversely, a 50% fill ratio significantly reduced production costs, but at the expense of mechanical performance. Thus, if strength is the primary requirement, a higher fill ratio is recommended. The effect of printing speed was found to be less significant compared to layer height and filler ratio. The maximum recorded tensile strength was 540.65 N, achieved with a layer height of 0.5 mm, a 100% fill ratio, and a printing speed of 8 mm/s. In contrast, the lowest recorded tensile strength was 389.93 N, observed with a layer height of 0.4 mm, a 50% fill ratio, and a printing speed of 4 mm/s. After applying a transformation function, the data showed good alignment with the normal distribution on the probability plot, indicating that the assumption of normality was satisfied. Additionally, the incorporation of glass fibers significantly enhanced the mechanical strength of the printed samples. Full article
(This article belongs to the Special Issue Recent Progress in Hybrid Composites)
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<p>Printing setup.</p>
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<p>Shows the standard sample design and the printed sample.</p>
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<p>Scatter plot of probability data for force response.</p>
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<p>Internal student’s residuals plot for the number of experiments for force response.</p>
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<p>(<b>a</b>) A 3D and (<b>b</b>) 2D diagram with the color spectrum of the infill change ratio–print speed on force.</p>
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<p>(<b>a</b>) A 3D and (<b>b</b>) 2D diagram with the color spectrum of the ratio of layer height changes–infill on force.</p>
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<p>The 3D and 2D charts with a color spectrum represent the layer height variation ratio to speed on the force (<b>a</b>) 3D and (<b>b</b>) 2d images.</p>
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<p>Optimal values suggested by Design Expert software.</p>
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<p>The fracture surface of non-reinforced PLA sample, (<b>A</b>) microscopic image, (<b>B</b>) the external appearance, and (<b>C</b>) the energy curve.</p>
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<p>The fracture surface of a fiber-reinforced PLA sample printed at a 4 mm/s speed, with a 0.6 mm layer height and a 100% filler ratio. (<b>A</b>) Micrograph; (<b>B</b>) external appearance of the fracture; (<b>C</b>) energy curve.</p>
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<p>The fracture surface of a fiber-reinforced PLA sample printed at an 8 mm/s speed, with a 0.5 mm nozzle and a 100% filler ratio. (<b>A</b>) Micrograph; (<b>B</b>) external appearance of the fracture; (<b>C</b>) energy curve.</p>
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<p>The fracture surface of a fiber-reinforced PLA sample printed at an 8 mm/s speed, with a 0.5 mm nozzle and a 75% filler ratio. (<b>A</b>) Micrograph; (<b>B</b>) external appearance of the fracture; (<b>C</b>) energy curve.</p>
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18 pages, 4260 KiB  
Article
Influence of Synthesis Conditions on the Structure, Composition, and Electromagnetic Properties of FeCoSm/C Nanocomposites
by Dmitriy Muratov, Lev Kozhitov, Irina Zaporotskova, Alena Popkova, Evgeniy Korovin, Sergey Boroznin and Natalia Boroznina
J. Compos. Sci. 2025, 9(2), 62; https://doi.org/10.3390/jcs9020062 - 1 Feb 2025
Abstract
New materials are actively being developed for use in various fields of electronics, as they can significantly improve the performance of electronic devices and prevent adverse effects. Such materials include nanocomposites, which include nanoparticles of magnetic metals and alloys in a non-magnetic polymer [...] Read more.
New materials are actively being developed for use in various fields of electronics, as they can significantly improve the performance of electronic devices and prevent adverse effects. Such materials include nanocomposites, which include nanoparticles of magnetic metals and alloys in a non-magnetic polymer or carbon matrix. For the first time, we synthesized FeCoSm/C nanocomposites and studied the effect of synthesis conditions on their structure, composition, and electromagnetic properties. Thermogravimetric (TG) analysis and differential scanning calorimetry (DSC) analysis of the heating processes of nanocomposite precursors allowed optimizing the mode of IR processing of precursors. X-ray phase analysis (XPA) showed that nanoparticles of a solid-metal solution based on the FeCo structure are formed, and at temperatures above 700 °C, the formation of SmCo5-x alloy nanoparticles is also possible. As the synthesis temperature increases, the average size of nanoparticles of alloys containing Sm increases. The effect of the metal ratio in the precursor on the structure, composition, and electromagnetic properties of FeCoSm/C nanocomposites is analyzed. It has been established that the most promising of all the studied materials are those obtained at a temperature of 700 °C with a metal ratio of Fe:Co:Sm = 50:40:10. Full article
(This article belongs to the Special Issue Recent Progress in Hybrid Composites)
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Figure 1
<p>(<b>a</b>) Change in the mass of precursors of the FeCoSm/C nanocomposite during IR heat treatment, (<b>b</b>) temperature dependences of the derivative of the degree of transformation for precursors relative to PAN.</p>
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<p>Diffractogram of the FeCoSm/C nanocomposite synthesized at T = 300 °C.</p>
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<p>Diffractograms of FeCoSm/C nanocomposites synthesized in the temperature range from 600 to 800 °C (the ratio of Fe:Co:Sm metals is indicated in parentheses). *—The positions of the reflexes of the oxide phase.</p>
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<p>Enlarged areas of diffractograms of FeCoSm/C nanocomposites synthesized in the temperature range from 600 to 800 °C, containing phase composition analysis: peak of the plane (110) of the FeCo phase (<b>a</b>); the area of angles where the reflexes of the oxide phases and carbon are visible (<b>b</b>).</p>
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<p>Dependence of the average size of the BCC of metal nanoparticles, based on the FeCo or Co lattice (300 °C), on the synthesis temperature.</p>
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<p>Diffractograms of FeCoSm/C nanocomposites synthesized in the temperature range from 600 to 800 °C; enlarged diffractogram area with phase composition analysis.</p>
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<p>(<b>a</b>) Diffractograms of two compositions of FeCoSm/C nanocomposites: 50:40:10 and 30:30:40; (<b>b</b>) angle range 2θ from 65° to 75° diffractograms of FeCoSm/C nanocomposites with metal ratio FeCoSm = 30:30:40.</p>
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<p>Raman spectra of PPAN and FeCoSm/C samples synthesized at 700 °C.</p>
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<p>Raman spectra of FeCoSm/C nanocomposites synthesized at various temperatures (for comparison, the spectra of PPAN and FeCo/C nanocomposite are given).</p>
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<p>Deconvolution of Raman spectra of nanocomposites at various temperatures: (<b>a</b>) FeCoSm/C at 600 °C; (<b>b</b>) FeCoSm/C at 700 °C; (<b>c</b>) FeCoSm/C at 800 °C; (<b>d</b>) Fe:Co:Sm = 40:40:20 at 700 °C; (<b>e</b>) PPAN at 700 °C; (<b>f</b>) FeCo/C at 700 °C. Fe and PAN obtained at various temperatures. Deconvolution of Raman spectra of nanocomposites and PPANS obtained at different temperatures.</p>
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<p>Frequency dependences on the ratio of metals in the precursor of the (<b>a</b>) complex dielectric, (<b>b</b>) magnetic, (<b>c</b>) permeability and tangent of dielectric, (<b>d</b>) magnetic losses.</p>
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<p>Optimization of the thickness of the absorber layer (<b>a</b>); frequency dependences of the reflection coefficient of nanocomposites (Tsint. = 700 °C) with a different ratio of metals in the precursor Fe:Co:Sm: 40:40:20 (<b>b</b>), 50:40:10 (<b>c</b>).</p>
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