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40 pages, 2817 KiB  
Review
Recent Advances in Fire Safety of Carbon Fiber-Reinforced Epoxy Composites for High-Pressure Hydrogen Storage Tanks
by Omar Dagdag and Hansang Kim
Polymers 2024, 16(23), 3343; https://doi.org/10.3390/polym16233343 - 28 Nov 2024
Abstract
The increasing use of hydrogen as a clean energy carrier has underscored the necessity for advanced materials that can provide safe storage under extreme conditions. Carbon fiber-reinforced epoxy (CFRP) composites are increasingly utilized in various high-performance applications, including automotive, aerospace, and particularly hydrogen [...] Read more.
The increasing use of hydrogen as a clean energy carrier has underscored the necessity for advanced materials that can provide safe storage under extreme conditions. Carbon fiber-reinforced epoxy (CFRP) composites are increasingly utilized in various high-performance applications, including automotive, aerospace, and particularly hydrogen storage tanks, due to their exceptional strength-to-weight ratio, durability, excellent corrosion resistance, and low thermal conductivity. However, the inherent flammability of epoxy matrices poses significant safety concerns, particularly in hydrogen storage, where safety is paramount. This review paper provides a comprehensive overview of the recent progress in enhancing the fire safety of CFRP. The focus is on innovative strategies such as developing novel flame-retardant (FR) additives, intumescent coatings, and nanomaterial reinforcements. It analyzes the effectiveness of these strategies in improving the fire performance of CFRP composites, including their flame retardancy, smoke suppression, and heat release rate reduction. The review paper also explores the application of fire modeling tools to predict the fire behavior of CFRP composite hydrogen storage tanks under various fire scenarios. Additionally, the review discusses the implications of these advancements on the performance and safety of hydrogen storage tanks, highlighting both the progress made and the challenges that remain. Full article
(This article belongs to the Special Issue Polymer Composite Analysis and Characterization II)
18 pages, 3048 KiB  
Article
Active Polypropylene Fibers for Controlling Shrinkage Cracks in Cement-Stabilized Materials
by Haibo Cao, Jing Li, Tuanjie Chen, Haisheng Ren and Zhu Qiao
Crystals 2024, 14(12), 1033; https://doi.org/10.3390/cryst14121033 - 28 Nov 2024
Abstract
Conventional polypropylene fibers, characterized by their smooth surfaces, exhibit relatively weak bonding with cement-based materials, limiting their effectiveness in enhancing these materials’ mechanical properties. This study investigates a graft-modified approach to activating polypropylene fibers, introducing amide groups onto their surfaces to improve fiber–matrix [...] Read more.
Conventional polypropylene fibers, characterized by their smooth surfaces, exhibit relatively weak bonding with cement-based materials, limiting their effectiveness in enhancing these materials’ mechanical properties. This study investigates a graft-modified approach to activating polypropylene fibers, introducing amide groups onto their surfaces to improve fiber–matrix interaction. The active polypropylene fibers were produced using an ultraviolet (UV) grafting technique, where maleic anhydride was first used to graft carboxyl groups onto the fiber surfaces, followed by acylation with diethylenetriamine to introduce amide bonds. The optimal experimental conditions were identified by using the degree of amidation as the response metric. Fourier-transform infrared (FTIR) spectroscopy and scanning electron microscopy (SEM) confirmed successful amination and surface activation, with a marked increase in specific surface area. The water contact angle of the active polypropylene fibers decreased significantly from 106.3° to 39.9°, indicating greatly improved wettability by the cement slurry and enhanced bonding strength between the fibers and the cement matrix. To evaluate the effects of the modified fibers, cement-stabilized macadam specimens incorporating various fiber contents were prepared and tested to determine their mechanical properties and shrinkage performance. The results indicated that, compared to conventional polypropylene fibers, the activated polypropylene fibers increased the 28-day compressive strength of CSM by 6.56%, enhanced tensile strength by 4.94%, reduced the rebound modulus by 7.42%, decreased the drying shrinkage coefficient by 25.55%, and lowered the thermal shrinkage coefficient by 13.16%. These findings demonstrate that the chemical bonding between the active polypropylene fibers and the cement matrix is significantly enhanced, leading to improved overall performance in crack resistance, material toughening, and shrinkage mitigation. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
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Figure 1
<p>Ultraviolet grafting process of maleic anhydride onto polypropylene fibers.</p>
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<p>Activation process of polypropylene fiber grafts.</p>
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<p>FTIR spectra of fibers.</p>
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<p>SEM images of fibers before and after modifications.</p>
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<p>Water contact angle of fibers.</p>
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<p>Microscopic morphology of fiber-enhanced cement-stabilized macadam specimens. (<b>a</b>) is cement-stabilized macadam specimens with ordinary polypropylene fibers; (<b>b</b>) is cement-stabilized macadam specimens with active polypropylene fibers.</p>
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<p>Trend of compressive strength.</p>
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<p>Trend of tensile strength.</p>
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<p>Trend of flexural tensile strength.</p>
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<p>Trend of rebound modulus.</p>
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<p>Dry shrinkage coefficient variation.</p>
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<p>Variation in temperature shrinkage coefficient.</p>
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20 pages, 7244 KiB  
Article
Small-Scale and Large-Scale Modeling of Fiber-Reinforced Concrete Girders
by Aleksandar Landović, Arpad Čeh, Anka Starčev-Ćurčin and Miloš Šešlija
Buildings 2024, 14(12), 3812; https://doi.org/10.3390/buildings14123812 - 28 Nov 2024
Abstract
Experimental and computational research on the behavior of small-scale and large-scale fiber-reinforced concrete (FRC) beams is presented in this paper. The experimental part included the small-scale bending tests, which were conducted on three 1.3 m long by 0.1 m wide by 0.15 m [...] Read more.
Experimental and computational research on the behavior of small-scale and large-scale fiber-reinforced concrete (FRC) beams is presented in this paper. The experimental part included the small-scale bending tests, which were conducted on three 1.3 m long by 0.1 m wide by 0.15 m high rectangular simply supported beams, and the large-scale test that was conducted on 12.8 m long by 0.2 m wide by 1.3 m two-chords girder. The concrete mixture in the large-scale test was designed with environmentally more justifiable supplementary materials (binder and fibers), striving for sustainable excellence. To accurately predict the mechanical behavior of tested models, a numerical model incorporating the real nonlinear materials laws is used. A numerical model based on finite element analysis (FEA) is developed. The FEA model is created using a smeared crack approach with a constitutive law for the tensile behavior of FRC derived from an inverse analysis based on prism bending tests. The numerical model is validated against experimental results and the accuracy of numerical predictions based on finite element modeling showed a good correlation with the test data. The FEA-based model makes it easier to predict how FRC structures fail under transversal loading and can serve as a foundation for creating new design processes. Additionally, the presented research is aimed at the feasibility of recycled steel FRC field application in building structures. The usage of recycled steel fibers could achieve environmental benefits through the adoption of sustainable materials. The present study showcased the possibility of modeling reinforced concrete structural building parts made with recycled steel fibers using available software. Full article
(This article belongs to the Section Building Structures)
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<p>Dimensions of the beam and reinforcement.</p>
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<p>(<b>a</b>) Test setup of the beam; (<b>b</b>) cracks on the side of the beam; (<b>c</b>) crack at failure.</p>
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<p>The geometry of the girder.</p>
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<p>Reinforcement of the girder.</p>
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<p>(<b>a</b>) Applied recycled steel fibers; (<b>b</b>) distribution of recycled steel fibers in concrete.</p>
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<p>Girder with second-phase loading.</p>
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<p>(<b>a</b>) Lifting of the support; (<b>b</b>) cracks in the final load phase at the measuring Point G; (<b>c</b>) cracks in the final load phase at the measuring Point A.</p>
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<p>Crack distribution and width in the final load phase.</p>
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<p>Finite element mesh, supports, and loading.</p>
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<p>Schematic representation of the maximum load.</p>
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<p>Reactions of a continuous beam due to unit distributed load.</p>
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<p>Finite element mesh, supports, and loading of the large girder.</p>
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<p>Stress–strain relationship of reinforcing steel.</p>
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<p>Stress–strain response of FRC in tension.</p>
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<p>Relationship between load and deflection at the mid-span: (<b>a</b>) experimental and FEM results; (<b>b</b>) characteristic points from FEM analysis.</p>
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<p>Normal stresses in beam: (<b>a</b>) before crack development; (<b>b</b>) after crack development.</p>
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<p>Cracks in beam at peak load.</p>
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<p>Normal stresses in reinforcement at peak load.</p>
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<p>Relationship between load and deflection at the mid-span.</p>
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<p>Deformations of the girder: (<b>a</b>) at service load; (<b>b</b>) at peak load.</p>
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<p>Normal stresses in girder.</p>
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<p>Cracks due to self-weight and maximal experimental load.</p>
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<p>Cracks in beam at peak load.</p>
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15 pages, 3830 KiB  
Article
Preparation of Hot-Pressed Wheat Straw Board by Self-Adhesive Process: Effects of Raw Material Sizes and Acid/Alkali Pretreatment
by Jianing Wang, Ziyue Feng, Jiachen Zuo, Qinzhen Fan and Libo Zhang
Materials 2024, 17(23), 5845; https://doi.org/10.3390/ma17235845 - 28 Nov 2024
Abstract
The development of wheat straw boards utilizing intrinsic bonding mechanisms not only facilitates the high-value utilization of agricultural solid waste but also diminishes the reliance on synthetic adhesives. In this study, using wheat straw as the primary substrate, we investigated the effects of [...] Read more.
The development of wheat straw boards utilizing intrinsic bonding mechanisms not only facilitates the high-value utilization of agricultural solid waste but also diminishes the reliance on synthetic adhesives. In this study, using wheat straw as the primary substrate, we investigated the effects of mechanical smashing combined with pretreatment using inorganic acids or alkalis on the properties of hot-pressed boards, as well as the relationship between the properties of hot-pressed boards and the physical properties and chemical composition of wheat straw raw materials. These selective pretreatments effectively degraded lignin, hemicellulose, and other components, thereby promoting fiber reorientation and resulting in a denser microstructure with improved self-bonding capabilities. The optimal board was fabricated with a granularity of 0.3 mm and underwent alkali pretreatment, achieving a tensile strength of 11.564 MPa, an internal bonding strength of 0.556 MPa, and bending strength and modulus of 24.306 MPa and 2.766 GPa, respectively. These findings have significant implications for advancing manufacturing processes and conceptualizing binder-free boards derived from agricultural residues. Full article
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Figure 1
<p>Experimental process for preparing hot-pressed wheat straw boards with different pretreatment methods and particle sizes.</p>
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<p>Macroscopic morphology of wheat straw with different pretreatment methods and raw material. (<b>a</b>) Untreated wheat straw. (<b>b</b>) Wheat straw pretreated with dilute acid. (<b>c</b>) Wheat straw pretreated with alkali.</p>
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<p>Microscopic morphology of the surface of hot-pressed wheat straw boards with different pretreatments and raw material sizes. (<b>a</b>) WS-5. (<b>b</b>) WS-3. (<b>c</b>) WS-1. (<b>d</b>) WS-Acid-5. (<b>e</b>) WS-Acid-3. (<b>f</b>) WS-Acid-1. (<b>g</b>) WS-Alkali-5. (<b>h</b>) WS-Alkali-3. (<b>i</b>) WS-Alkali-1.</p>
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<p>Chemical structure characterization of hot-pressed wheat straw boards with different pretreatments. (<b>a</b>,<b>b</b>) FTIR spectra. (<b>c</b>) Chemical composition graph. (<b>d</b>) XRD spectra.</p>
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<p>(<b>a</b>) X-Ray photoelectron spectroscopy (XPS) spectra. (<b>b</b>) C 1s X-Ray photoelectron spectroscopy (XPS) spectra.</p>
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<p>Physical and mechanical properties of hot-pressed wheat straw boards with different pretreatment methods and raw material sizes. (<b>a</b>) Tensile strength. (<b>b</b>) Internal bonding strength. (<b>c</b>) Bending strength and modulus of elasticity. (<b>d</b>) Water absorption rate.</p>
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<p>Water absorption rate of hot-pressed wheat straw boards with different pretreatment methods and raw material sizes.</p>
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<p>Thermogravimetric analysis of hot-pressed wheat straw boards with different pretreatment methods. (<b>a</b>) Thermogravimetric analysis (TG). (<b>b</b>) Differential thermogravimetric analysis (DTG).</p>
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23 pages, 8761 KiB  
Article
Structural Optimization of a High-Performance Green Sandwich Made of Sisal Reinforced Epoxy Facings and Balsa Core
by Bernardo Zuccarello, Francesco Bongiorno and Carmelo Militello
Polymers 2024, 16(23), 3341; https://doi.org/10.3390/polym16233341 - 28 Nov 2024
Viewed by 58
Abstract
Within the range of composite laminates for structural applications, sandwich laminates are a special category intended for applications characterized by high flexural stresses. As it is well known from the technical literature, structural sandwich laminates have a simple configuration consisting of two skins [...] Read more.
Within the range of composite laminates for structural applications, sandwich laminates are a special category intended for applications characterized by high flexural stresses. As it is well known from the technical literature, structural sandwich laminates have a simple configuration consisting of two skins of very strong material, to which the flexural strength is delegated, between which an inner layer (core) of light material with sufficient shear strength is interposed. As an example, a sandwich configuration widely used in civil, naval, and mechanical engineering is that obtained with fiberglass skins and a core of various materials, such as polyurethane foam or another lightweight material, depending on the application. Increasingly stringent regulations aimed at protecting the environment by reducing harmful emissions of carbon dioxide and carbon monoxide have directed recent research towards the development of new composites and new sandwiches characterized by low environmental impact. Among the various green composite solutions proposed in the literature, a very promising category is that of high-performance biocomposites, which use bio-based matrices reinforced by fiber reinforcements. This approach can also be used to develop green sandwiches for structural applications, consisting of biocomposite skins and cores made by low-environmental impact or renewable materials. In order to make a contribution to this field, a structural sandwich consisting of high-performance sisal–epoxy biocomposite skins and an innovative renewable core made of balsa wood laminates with appropriate lay-ups has been developed and then properly characterized in this work. Through a systematic theoretical–experimental analysis of three distinct core configurations, the unidirectional natural core, the cross-ply type, and the angle-ply type, it has been shown how the use of natural balsa gives rise to inefficient sandwiches, whereas performance optimization is fully achieved by considering the angle-ply core type [±45/90]. Finally, the subsequent comparison with literature data of similar sandwiches has shown how the optimal configuration proposed can be advantageously used to replace synthetic glass–resin sandwiches widely used in various industrial sectors (mechanical engineering, shipbuilding, etc.) and in civil engineering. Full article
(This article belongs to the Section Polymer Fibers)
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Figure 1
<p>Balsa core with fibers at (<b>a</b>) 0°—called B(0), (<b>b</b>) ±45°—called B(±45), and (<b>c</b>) ±45°/90°—called B(±45/90).</p>
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<p>Innovative balsa laminate core type B(±45/90).</p>
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<p>Sandwich samples manufactured in the laboratory: (<b>a</b>) SB(0), (<b>b</b>) SB(±45), (<b>c</b>) SB(±45/90).</p>
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<p>Longitudinal tensile curves for four skin specimens tested and their average curve.</p>
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<p>Average flatwise compression curves of the tested specimens B(0), B(±45), and B(±45/90).</p>
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<p>Typical fractures of core specimens tested in flatwise compression: (<b>a</b>) B(0), (<b>b</b>) B(±45), (<b>c</b>) B(±45/90).</p>
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<p>Average shear curves for sandwiches SB(0), SB(±45), and SB(±45/90).</p>
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<p>Shear failure of the sandwich core: (<b>a</b>) SB(0)<sub>10</sub>, (<b>b</b>) SB(±45)<sub>10,</sub> and (<b>c</b>) SB(±45/90)<sub>10</sub>.</p>
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<p>Flexural test of the SB(0)<sub>25</sub> sandwich (<b>a</b>) flexural curve, (<b>b</b>) specimen at failure.</p>
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<p>Flexural test of the SB(0)<sub>10</sub> sandwich: (<b>a</b>) flexural curve, (<b>b</b>) specimen during, and (<b>c</b>) after the test.</p>
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<p>Flexural test of the SB(±45)<sub>25</sub> sandwich: (<b>a</b>) flexural curve, (<b>b</b>) specimen during the test, and (<b>c</b>) after tensile failure of the lower skin.</p>
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<p>Flexural test of the SB(±45)<sub>10</sub> sandwich: (<b>a</b>) flexural curve, (<b>b</b>) specimen during the test, and (<b>c</b>) after compression buckling of the upper skin.</p>
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<p>Sandwich flexural test SB(±45/90)<sub>25</sub>: (<b>a</b>) flexural curve, (<b>b</b>) specimen during the test, and (<b>c</b>) after shear failure of the core.</p>
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<p>Flexural test of the SB(±45/90)<sub>10</sub> sandwich: (<b>a</b>) flexural curve, (<b>b</b>) specimen during the test, and (<b>c</b>) after shear failure of the core.</p>
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<p>Comparison of the skin stress of the proposed green sandwich with that of other sandwiches reported in the literature [<a href="#B5-polymers-16-03341" class="html-bibr">5</a>,<a href="#B8-polymers-16-03341" class="html-bibr">8</a>,<a href="#B30-polymers-16-03341" class="html-bibr">30</a>,<a href="#B31-polymers-16-03341" class="html-bibr">31</a>,<a href="#B32-polymers-16-03341" class="html-bibr">32</a>,<a href="#B33-polymers-16-03341" class="html-bibr">33</a>,<a href="#B34-polymers-16-03341" class="html-bibr">34</a>,<a href="#B35-polymers-16-03341" class="html-bibr">35</a>,<a href="#B36-polymers-16-03341" class="html-bibr">36</a>,<a href="#B37-polymers-16-03341" class="html-bibr">37</a>,<a href="#B38-polymers-16-03341" class="html-bibr">38</a>,<a href="#B39-polymers-16-03341" class="html-bibr">39</a>,<a href="#B40-polymers-16-03341" class="html-bibr">40</a>,<a href="#B41-polymers-16-03341" class="html-bibr">41</a>,<a href="#B42-polymers-16-03341" class="html-bibr">42</a>,<a href="#B43-polymers-16-03341" class="html-bibr">43</a>,<a href="#B44-polymers-16-03341" class="html-bibr">44</a>].</p>
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<p>Comparison of the specific stress of the optimal green sandwich with that of other sandwiches reported in the literature [<a href="#B5-polymers-16-03341" class="html-bibr">5</a>,<a href="#B8-polymers-16-03341" class="html-bibr">8</a>,<a href="#B30-polymers-16-03341" class="html-bibr">30</a>,<a href="#B31-polymers-16-03341" class="html-bibr">31</a>,<a href="#B32-polymers-16-03341" class="html-bibr">32</a>,<a href="#B33-polymers-16-03341" class="html-bibr">33</a>,<a href="#B34-polymers-16-03341" class="html-bibr">34</a>,<a href="#B35-polymers-16-03341" class="html-bibr">35</a>,<a href="#B36-polymers-16-03341" class="html-bibr">36</a>,<a href="#B37-polymers-16-03341" class="html-bibr">37</a>,<a href="#B38-polymers-16-03341" class="html-bibr">38</a>,<a href="#B39-polymers-16-03341" class="html-bibr">39</a>,<a href="#B40-polymers-16-03341" class="html-bibr">40</a>,<a href="#B41-polymers-16-03341" class="html-bibr">41</a>,<a href="#B42-polymers-16-03341" class="html-bibr">42</a>,<a href="#B43-polymers-16-03341" class="html-bibr">43</a>,<a href="#B44-polymers-16-03341" class="html-bibr">44</a>].</p>
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<p>Comparison of the flexural modulus of the proposed green sandwich with that of other sandwiches reported in the literature [<a href="#B8-polymers-16-03341" class="html-bibr">8</a>,<a href="#B31-polymers-16-03341" class="html-bibr">31</a>,<a href="#B33-polymers-16-03341" class="html-bibr">33</a>,<a href="#B35-polymers-16-03341" class="html-bibr">35</a>,<a href="#B37-polymers-16-03341" class="html-bibr">37</a>,<a href="#B38-polymers-16-03341" class="html-bibr">38</a>,<a href="#B39-polymers-16-03341" class="html-bibr">39</a>,<a href="#B40-polymers-16-03341" class="html-bibr">40</a>,<a href="#B42-polymers-16-03341" class="html-bibr">42</a>,<a href="#B43-polymers-16-03341" class="html-bibr">43</a>,<a href="#B44-polymers-16-03341" class="html-bibr">44</a>].</p>
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<p>Comparison of the specific flexural modulus of the proposed green sandwich with that of other sandwiches reported in the literature [<a href="#B8-polymers-16-03341" class="html-bibr">8</a>,<a href="#B31-polymers-16-03341" class="html-bibr">31</a>,<a href="#B33-polymers-16-03341" class="html-bibr">33</a>,<a href="#B35-polymers-16-03341" class="html-bibr">35</a>,<a href="#B37-polymers-16-03341" class="html-bibr">37</a>,<a href="#B38-polymers-16-03341" class="html-bibr">38</a>,<a href="#B39-polymers-16-03341" class="html-bibr">39</a>,<a href="#B40-polymers-16-03341" class="html-bibr">40</a>,<a href="#B42-polymers-16-03341" class="html-bibr">42</a>,<a href="#B43-polymers-16-03341" class="html-bibr">43</a>,<a href="#B44-polymers-16-03341" class="html-bibr">44</a>].</p>
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<p>Sandwich panel sketch with geometrical and load notations.</p>
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14 pages, 17007 KiB  
Article
Study of the Influence of Bamboo Suspension Water-Removal Processes on the Properties of Bamboo-Based Molding Materials
by Xiaowei Zhuang, Weichen Li, Xin Pan, Hui Qiao, Baoyong Liu, Weiming Yang and Yongshun Feng
Polymers 2024, 16(23), 3337; https://doi.org/10.3390/polym16233337 - 28 Nov 2024
Viewed by 86
Abstract
Bamboo is a fast-growing lignocellulosic plant in nature. It is an abundant and renewable resource with wide applications. The processing of bamboo results in a large amount of residue. In this paper, we developed a method to utilize bamboo residue to prepare a [...] Read more.
Bamboo is a fast-growing lignocellulosic plant in nature. It is an abundant and renewable resource with wide applications. The processing of bamboo results in a large amount of residue. In this paper, we developed a method to utilize bamboo residue to prepare a novel lightweight porous molding material. A hydrated thermochemical grinding process was proposed to disintegrate bamboo fibers and activate bamboo’s own binding components. The influence of the water removal by pressure from bamboo suspension and subsequent different drying methods on the product’s properties was evaluated. The two-step drying ensured a low production cost and high product quality. The bamboo molding material was characterized based on thermal stability, morphology, functional groups, particle size distribution, crystallinity, and mechanical strength. A lightweight porous material was obtained with a density of 0.23–0.35 g/cm3 by freeze-drying. A high mechanical strength was obtained with a tensile strength of 0.62 MPa and a compressive strength of 10.31 MPa by oven drying. The auto-adhesive mechanisms, including fiber anchorage, polymerization, water plasticization, and heat plasticization, were discussed. The bamboo molding material is a reconstruction of bamboo cell wall components and is easy to recycle. It has potential applications in construction and buildings, packaging, and indoor furnishings. Full article
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Figure 1
<p>Schematic illustration of the preparation of bamboo-based molding materials.</p>
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<p>Pyrolysis characteristics of bamboo before and after HTG process.</p>
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<p>FTIR spectra of bamboo samples.</p>
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<p>X-ray diffraction of bamboo samples.</p>
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<p>SEM images of bamboo powder before and after HTG process.</p>
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<p>Distribution of particle size in the bamboo suspension after HTG process.</p>
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<p>Water removal with different pressures.</p>
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<p>Weight loss of porous bamboo mold after freeze drying at −60 °C (<b>A</b>) and drying at 80 °C (<b>B</b>) as a function of time and pressure.</p>
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<p>Relationship between pressure and density of bamboo-based porous molding materials under freeze drying and conventional oven drying.</p>
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<p>Mechanical performance of bamboo-based molding materials: (<b>A</b>) Tensile strength; (<b>B</b>) Compressive strength; (<b>C</b>) Impact energy; (<b>D</b>) Young’s modulus; (<b>E</b>) Bending strength; (<b>F</b>) Schore hardness.</p>
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15 pages, 5434 KiB  
Article
High Absorption and Elasticity of a Novel Transgenic Silk with Egg Case Silk Protein from Nephila clavata
by Yichen Wang, Yuhang Lin, Yongkang Luo, Di Zeng, Haibo He and Tianfu Zhao
Int. J. Mol. Sci. 2024, 25(23), 12793; https://doi.org/10.3390/ijms252312793 - 28 Nov 2024
Viewed by 81
Abstract
Spider silk is part of a special class of natural protein fibers that have high strength and toughness: these materials have excellent comprehensive properties that are not found in other natural fibers (including silk) or most synthetic fibers. Spider egg case filaments have [...] Read more.
Spider silk is part of a special class of natural protein fibers that have high strength and toughness: these materials have excellent comprehensive properties that are not found in other natural fibers (including silk) or most synthetic fibers. Spider egg case filaments have good hardness, can resist water, can protect spider eggs from external threats, have a significantly high initial modulus and high moisture absorption rate, and are expected to be used as a new generation of environmentally friendly natural polymer fibers and biomaterials. However, spiders are predatory and difficult to rear in large numbers, and it is also difficult to obtain spider egg case filaments in large quantities. Silkworms and spiders have a similar spinning system, and the use of transgenic technology in silkworms can obtain stable and high-yield exogenous gene proteins for a long time, representing an ideal bioreactor for the production of spider silk. In this study, the eukaryotic bioreactor and piggyBac transposon system were employed to recombinantly introduce the egg case silk protein of Nephila clavata (Nc-CYSP1) into the silkworm in the silkworm heavy-chain expression system. The results revealed that the silk glands produced a new type of transgenic silk with a significantly high initial modulus and high moisture absorption. In summary, this study provides an experimental reference for future research on the large-scale production and application of spider egg case filamentous protein, with great application prospects in the development of new environmentally friendly materials. Full article
(This article belongs to the Section Molecular Biology)
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<p>Optimally designed spider egg case silk: basic unit.</p>
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<p>Schematic diagram of vector construction: (<b>A</b>) the cloning vector with quadruple target genes; (<b>B</b>) the shuttle vector with a quadruple gene of interest; and (<b>C</b>) the <span class="html-italic">piggy</span>Bac transposable vector with the quadruple target gene.</p>
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<p>Vector pBAC-3xP3-DsRed-FibH-<span class="html-italic">Nc</span>-4xCYSP1-LBS and enzyme digestion validation. M: DL5000Marker; 1: vector pBAC-3xP3-DsRed-FibH-<span class="html-italic">Nc</span>-4xCYSP1-LBS; 2: vector pBAC-3xP3-DsRed-FibH-<span class="html-italic">Nc</span>-4xCYSP1-LBS enzyme digestion.</p>
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<p>Comparison chart of a transgenic positive silkworm moth in various periods; wild-type WT and G1 egg (<b>a1</b>,<b>b1</b>), larval (<b>a2</b>,<b>b2</b>), pupal (<b>a3</b>,<b>b3</b>), and moth (<b>a4</b>,<b>b4</b>) stages, respectively, were observed under red fluorescence. It can be observed that only transgenic positive silkworms can specifically express the DsRed gene at the egg, larval, pupal, and moth stages and red fluorescence in the eyes.</p>
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<p>Insertion site analysis of transgenic silkworms. (<b>A</b>) Distribution of insertion sites of transgenic silkworms. (<b>B</b>) Specific insertion sequences of transgenic silkworms.</p>
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<p>Results of relative mRNA expression. WT: D9L genetically unmodified silkworm. CYSP1: Genetically modified silkworms. Three biological replicates per sample, using the two-tailed test mode: ** means <span class="html-italic">p</span> &lt; 0.01 and * indicates <span class="html-italic">p</span> &lt; 0.05.</p>
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<p>SDS-PAGE protein electrophoresis. M: protein molecular weight. 1: sample of common D9L silkworm cocoon protein. 2: A sample of silkworm cocoon protein from the egg case silk gene of <span class="html-italic">Nephila clavata</span>.</p>
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<p>Scanning electron microscope (SEM) images of silk fibers.</p>
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<p>FTIR results of silks.</p>
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<p>Infrared spectroscopy of amide I band peak-fitting results. (<b>A</b>) Undegummed cocoon silk. (<b>B</b>) Undegummed transgenic cocoon silk. (<b>C</b>) Degummed common cocoon silk. (<b>D</b>) Degummed transgenic cocoon silk. (<b>E</b>) The egg case silk filament protein from <span class="html-italic">Nephila clavata</span>.</p>
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<p>Stress–strain curves of different silk strains: (<b>A</b>) all silk strains, (<b>B</b>) undegummed cocoon silk, (<b>C</b>) degummed cocoon silk, (<b>D</b>) undegummed transgenic cocoon silk, and (<b>E</b>) degummed transgenic cocoon silk.</p>
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<p>Histograms of the (<b>A</b>) Young’s modulus and (<b>B</b>) toughness of different silk strains.</p>
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12 pages, 14552 KiB  
Article
Cellulose-Based Acoustic Absorber with Macro-Controlled Properties
by Jérôme Lefebvre, Benoit Genestie and Alexandre Leblanc
Acoustics 2024, 6(4), 1088-1099; https://doi.org/10.3390/acoustics6040059 - 28 Nov 2024
Viewed by 63
Abstract
Cellulose-based materials are now commonly used, including in the field of acoustic comfort. Often presented as a less environmentally impactful alternative to traditional acoustic absorbents (such as melamine, glass wool, etc.), these cellulose-based materials are more frequently derived from recycling, undergoing, in most [...] Read more.
Cellulose-based materials are now commonly used, including in the field of acoustic comfort. Often presented as a less environmentally impactful alternative to traditional acoustic absorbents (such as melamine, glass wool, etc.), these cellulose-based materials are more frequently derived from recycling, undergoing, in most cases, a technical process that allows these cellulose fibers to be obtained, thus inheriting the acoustic properties of the latter, with limited or even non-existent control. This paper proposes a manufacturing process that allows for the production of cellulose foam with precise control over its porosity, pore size, and interconnections. In addition to exhibiting good sound absorption properties, this process also enables the fabrication of gradient-porous structures and other hybrid materials, which can result in remarkable sound absorption properties. Full article
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<p>(<b>a</b>) shrunk PMMA beads and (<b>b</b>) resulting porous ceramic [<a href="#B28-acoustics-06-00059" class="html-bibr">28</a>].</p>
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<p>Construction of the frame with PMMA beads.</p>
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<p>Synopsis of the manufacturing process.</p>
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<p>(<b>a</b>) The 6 samples characterized in <a href="#acoustics-06-00059-t001" class="html-table">Table 1</a> and (<b>b</b>) a microscopic view of one sample.</p>
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<p>(<b>a</b>) Max/min and mean absorption coefficients of the 6 samples depicted in <a href="#acoustics-06-00059-t001" class="html-table">Table 1</a> and (<b>b</b>) the 5 samples depicted in <a href="#acoustics-06-00059-t002" class="html-table">Table 2</a>.</p>
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<p>(<b>a</b>) Absorption coefficient. (<b>b</b>) Microscopic view of porous cellulose with double porosity.</p>
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<p>First manufacturing step of gradient foams.</p>
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<p>Absorption coefficients of gradient-porous biomaterials.</p>
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<p>Pore-size estimation for the continuous interconnection gradient material acoustically characterized in <a href="#acoustics-06-00059-f008" class="html-fig">Figure 8</a>a.</p>
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<p>Pore-size estimation for the porosity gradient material acoustically characterized in <a href="#acoustics-06-00059-f008" class="html-fig">Figure 8</a>b.</p>
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23 pages, 6682 KiB  
Article
Machining Eco-Friendly Jute Fiber-Reinforced Epoxy Composites Using Specially Produced Cryo-Treated and Untreated Cutting Tools
by Mehmet Şükrü Adin and Hamit Adin
Polymers 2024, 16(23), 3329; https://doi.org/10.3390/polym16233329 - 27 Nov 2024
Viewed by 165
Abstract
In recent years, consumers have become increasingly interested in natural, biodegradable and eco-friendly composites. Eco-friendly composites manufactured using natural reinforcing filling materials stand out with properties such as cost effectiveness and easy accessibility. For these reasons, in this research, a composite workpiece was [...] Read more.
In recent years, consumers have become increasingly interested in natural, biodegradable and eco-friendly composites. Eco-friendly composites manufactured using natural reinforcing filling materials stand out with properties such as cost effectiveness and easy accessibility. For these reasons, in this research, a composite workpiece was specially manufactured using eco-friendly jute fibers. Two cost-effective cutting tools were specially produced to ensure high-quality machining of this composite workpiece. One of these specially manufactured cutting tools was subjected to DC&T (deep cryogenic treatment and tempering) processes to improve its performance. At the end of the research, when the lowest and highest Fd (delamination factor) values obtained with DC&T-T1 and T1 cutting tools were compared, it was observed that 5.49% and 6.23% better results were obtained with the DC&T-T1 cutting tool, respectively. From the analysis of the S/N (signal-to-noise) ratios obtained using Fd values, it was found that the most appropriate machining parameters for the composite workpiece used in this investigation were the DC&T-T1 cutting tool, a 2000 rev/min spindle speed and a 100 mm/min feed rate. Through ANOVAs (analyses of variance), it was discovered that the most significant parameter having an impact on the Fd values was the spindle speed, with a rate of 53.01%. Considering the lowest and highest Ra (average surface roughness) values obtained using DC&T-T1 and T1 cutting tools, it was seen that 19.42% and 16.91% better results were obtained using the DC&T-T1 cutting tool, respectively. In the S/N ratio analysis results obtained using Ra values, it was revealed that the most appropriate machining parameters for the composite workpiece used in this investigation were the DC&T-T1 cutting tool, a 2000 rev/min spindle speed and a 100 mm/min feed rate. In the ANOVAs, it was revealed that the most significant parameter having an effect on the Ra values was the feed rate at 37.86%. Full article
13 pages, 2817 KiB  
Article
Flammability and Thermoregulation Performance of Multilayer Protective Clothing Incorporated with Phase Change Materials
by Muhammad Shoaib, Hafsa Jamshaid, Rajesh Kumar Mishra, Kashif Iqbal, Miroslav Müller, Vijay Chandan and Tatiana Alexiou Ivanova
Materials 2024, 17(23), 5826; https://doi.org/10.3390/ma17235826 - 27 Nov 2024
Viewed by 451
Abstract
Firefighters need personal protection equipment and protective clothing to be safe and protected when responding to fire incidents. At present, firefighters’ suits are developed by using inherently thermal-resistant fibers but pose serious problems related to comfort. In the present research, multilayered fire-fighting fabrics [...] Read more.
Firefighters need personal protection equipment and protective clothing to be safe and protected when responding to fire incidents. At present, firefighters’ suits are developed by using inherently thermal-resistant fibers but pose serious problems related to comfort. In the present research, multilayered fire-fighting fabrics were developed with different fiber blends. Multilayer fire retardant (FR) fabrics with phase change materials (PCMs) inserts were developed and compared with reference multilayer fabrics without PCM. In this context, four fabric samples were chosen to fabricate the multilayer FR fabrics. Properties of multilayer fabrics were investigated, which include physical, thermo–physiological comfort, and flame-resistant performance. The heating process of the clothing was examined using infrared (IR) thermography, differential scanning calorimetry (DSC), thermal protective testing (TPP), and steady-state (Convective and Radiant) heat resistance tests. Areal density and thickness were measured as physical parameters, and air permeability (AP), overall moisture management capacity (OMMC), and thermal conductivity were measured as thermo–physiological comfort characteristics. The inclusion of PCM improved the thermal protection as well as flame resistance significantly. Sample S1 (Nomex + PTFE + Nomex with PCM) demonstrated superior fire resistance, air permeability, and thermal protection, with a 37.3% increase in air permeability as compared to the control sample (SC) by maintaining comfort while offering high thermal resilience. The inclusion of PCM enhanced its thermal regulation, moderating heat transfer. Flame resistance tests confirmed its excellent performance, while thermo–physiological assessments highlighted a well-balanced combination of thermal conductivity and air permeability. This study will help to improve the performance of firefighter protective fabrics and provide guidelines in terms of balancing comfort and performance while designing firefighter protective clothing for different climatic conditions. Full article
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<p>Schematic and assembly for the fabrication of multilayer firefighter suit.</p>
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<p>Instruments used for thermal testing of multilayer fabrics: (<b>a</b>) thermal protective tester, (<b>b</b>) Kawabata thermal conductivity tester, and (<b>c</b>) auto/horizontal flame tester.</p>
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<p>Multilayer fabrics after flame tests.</p>
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<p>PCM’s performance: (<b>a</b>) thermal images of multilayer fabrics at different residence times. (<b>b</b>) Enthalpy of PCMs.</p>
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<p>Comparison of thermal protective performance of the multilayer fabrics, S1, S2, S3, S4, SC, and barchart showing their thermal performance. The bars in <a href="#materials-17-05826-f005" class="html-fig">Figure 5</a> show mean values with standard deviation (SD). As can be seen, the trend of the protective performance of the prepared samples was S1 &gt; S3 &gt; S2 &gt; S4, respectively. As S1 and S3 samples consist of Nomex, which has inherently good char ability and creates a protective layer on the surface of the fabric, its thermal protective performance was better than other types of fibers used. Sample S4 showed the lowest thermal performance, which was also evident from the minimum char produced.</p>
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17 pages, 10313 KiB  
Article
Flexural Behavior of Innovative Glass Fiber-Reinforced Composite Beams Reinforced with Gypsum-Based Composites
by Yiwen Liu, Bo Su and Tianyu Zhang
Polymers 2024, 16(23), 3327; https://doi.org/10.3390/polym16233327 - 27 Nov 2024
Viewed by 206
Abstract
Glass Fiber-Reinforced Composite (GFRP) has found widespread use in engineering structures due to its lightweight construction, high strength, and design flexibility. However, pure GFRP beams exhibit weaknesses in terms of stiffness, stability, and local compressive strength, which compromise their bending properties. In addressing [...] Read more.
Glass Fiber-Reinforced Composite (GFRP) has found widespread use in engineering structures due to its lightweight construction, high strength, and design flexibility. However, pure GFRP beams exhibit weaknesses in terms of stiffness, stability, and local compressive strength, which compromise their bending properties. In addressing these limitations, this study introduces innovative square GFRP beams infused with gypsum-based composites (GBIGCs). Comprehensive experiments and theoretical analyses have been conducted to explore their manufacturing process and bending characteristics. Initially, four types of GBIGC—namely, hollow GFRP beams, pure gypsum, steel-reinforced gypsum, and fiber-mixed gypsum-infused beams—were designed and fabricated for comparative analysis. Material tests were conducted to assess the coagulation characteristics of gypsum and its mechanical performance influenced by polyvinyl acetate fibers (PVAs). Subsequently, eight GFRP square beams (length: 1.5 m, section size: 150 mm × 150 mm) infused with different gypsum-based composites underwent four-point bending tests to determine their ultimate bending capacity and deflection patterns. The findings revealed that a 0.12% dosage of protein retarder effectively extends the coagulation time of gypsum, making it suitable for specimen preparation, with initial and final setting times of 113 min and 135 min, respectively. The ultimate bending load of PVA-mixed gypsum-infused GFRP beams is 203.84% higher than that of hollow beams, followed by pure gypsum and steel-reinforced gypsum, with increased values of 136.97% and 186.91%, respectively. The ultimate load values from the theoretical and experimental results showed good agreement, with an error within 7.68%. These three types of GBIGCs with significantly enhanced flexural performance can be filled with different materials to meet specific load-bearing requirements for various scenarios. Their improved flexural strength and lightweight characteristics make GBIGCs well suited for applications such as repairing roof beams, light prefabricated frames, coastal and offshore buildings. Full article
(This article belongs to the Special Issue Application and Characterization of Polymer Composites)
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<p>GFRP beams and directions.</p>
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<p>Samples in two directions of GFRP.</p>
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<p>Gypsum coagulation tests.</p>
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<p>Manufacturing process of PVA gypsum blocks.</p>
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<p>The 50 T self-balancing device and layout of sensors.</p>
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<p>Relation between the retarder and the setting time of gypsum.</p>
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<p>Mechanical performance of PVA gypsum blocks.</p>
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<p>Loading of GFRP beams.</p>
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<p>Local failure pattern at loading points of hollow GFRP or GBIGC specimens.</p>
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<p>Mid-span deflection of test beams.</p>
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<p>Load–strain curves of different gauges.</p>
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<p>Strain distribution along web height.</p>
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37 pages, 15018 KiB  
Review
Graphene-Based Fiber Materials for Gas Sensing Applications: State of the Art Review
by Susanna Vu, Mohamed Siaj and Ricardo Izquierdo
Materials 2024, 17(23), 5825; https://doi.org/10.3390/ma17235825 - 27 Nov 2024
Viewed by 306
Abstract
The importance of gas sensors is apparent as the detection of gases and pollutants is crucial for environmental monitoring and human safety. Gas sensing devices also hold the potential for medical applications as health monitoring and disease diagnostic tools. Gas sensors fabricated from [...] Read more.
The importance of gas sensors is apparent as the detection of gases and pollutants is crucial for environmental monitoring and human safety. Gas sensing devices also hold the potential for medical applications as health monitoring and disease diagnostic tools. Gas sensors fabricated from graphene-based fibers present a promising advancement in the field of sensing technology due to their enhanced sensitivity and selectivity. The diverse chemical and mechanical properties of graphene-based fibers—such as high surface area, flexibility, and structural stability—establish them as ideal gas-sensing materials. Most significantly, graphene fibers can be readily tuned to detect a wide range of gases, making them highly versatile in gas-sensing technologies. This review focuses on graphene-based composite fibers for gas sensors, with an emphasis on the preparation processes used to achieve these fibers and the gas sensing mechanisms involved in their sensors. Graphene fiber gas sensors are presented based on the chemical composition of their target gases, with detailed discussions on their sensitivity and performance. This review reveals that graphene-based fibers can be prepared through various methods and can be effectively integrated into gas-sensing devices for a diverse range of applications. By presenting an overview of developments in this field over the past decade, this review highlights the potential of graphene-based fiber sensors and their prospective integration into future technologies. Full article
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<p>Examples of graphene-based fiber sensors for diatomic gases: (<b>a</b>) Schematic illustration of RGO-ZnO sensing mechanism for H<sub>2</sub> gas [<a href="#B69-materials-17-05825" class="html-bibr">69</a>]; (<b>b</b>) Schematic diagram of Cd/RGO/SnO<sub>2</sub> sensing mechanism to CO gas [<a href="#B73-materials-17-05825" class="html-bibr">73</a>].</p>
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<p>Schematic illustration of graphene/PANI/PS nanofibers preparation steps [<a href="#B91-materials-17-05825" class="html-bibr">91</a>].</p>
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<p>Field-emission scanning electron microscopy images of: (<b>a</b>) Pristine CuO nanofibers, and RGO-CuO nanofibers with different amounts of RGO; (<b>b</b>) 0.05 wt% RGO, (<b>c</b>) 0.1 wt% RGO, (<b>d</b>) 0.2 wt% RGO, (<b>e</b>) 0.3 wt% RGO, (<b>f</b>) 0.5 wt% RGO, (<b>g</b>) 1 wt% RGO, and (<b>h</b>) 1.5 wt RGO% [<a href="#B93-materials-17-05825" class="html-bibr">93</a>].</p>
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<p>Schematic illustration of the fabrication process for PS-WO<sub>3</sub>/NOGR nanofibers, whereby controlled pore distribution on the nanofiber is achieved [<a href="#B95-materials-17-05825" class="html-bibr">95</a>].</p>
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<p>Schematic depicting the gas sensing mechanism of RGO-ZnFe<sub>2</sub>O<sub>4</sub> nanofibers: (<b>a</b>) Band diagram of RGO and ZFO; (<b>b</b>) At equilibrium; (<b>c</b>) In air; (<b>d</b>) H<sub>2</sub>S gas exposure [<a href="#B98-materials-17-05825" class="html-bibr">98</a>].</p>
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<p>Schematic illustration of the sensing mechanism of (<b>a</b>) In<sub>2</sub>O<sub>3</sub> compared to (<b>b</b>) RGO-In<sub>2</sub>O<sub>3</sub> towards NO<sub>2</sub> gas [<a href="#B111-materials-17-05825" class="html-bibr">111</a>].</p>
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<p>(<b>a</b>) Response of RGO-SnO<sub>2</sub> nanofibers to NO<sub>2</sub>, O<sub>2</sub>, and SO<sub>2</sub> gases, where the concentration was set to of 1, 2, and 5 ppm, respectively [<a href="#B114-materials-17-05825" class="html-bibr">114</a>]; (<b>b</b>) Response of RGO-ZnO nanofibers, with varying RGO concentrations, to 5 ppm of NO<sub>2</sub> gas [<a href="#B70-materials-17-05825" class="html-bibr">70</a>].</p>
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<p>Schematic illustration of Cu/Cu<sub>2</sub>O/graphene and Ni/NiO/graphene fiber (M/MO/GF) fabrication, involving wet-spinning and thermal treatment of fibers [<a href="#B122-materials-17-05825" class="html-bibr">122</a>].</p>
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<p>Images of RGO/WO<sub>3</sub>/TCNF fibers integrated into various objects: (<b>a</b>) A wristwatch (the area highlighted in yellow is where the fiber was integrated); (<b>b</b>) A pair of safety goggles; (<b>c</b>) Sown onto Kimtech paper; (<b>d</b>) A wearable sensing module. NO<sub>2</sub> gas monitoring from the portable sensing device (<b>d</b>) is depicted in (<b>e</b>) [<a href="#B125-materials-17-05825" class="html-bibr">125</a>].</p>
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<p>(<b>a</b>) Schematic illustration depicting the multi-step fabrication of RGO/ZnO/thread sensors; (<b>b</b>) Image of sensor array network of RGO/ZnO/thread and its integration onto wearable fabric [<a href="#B128-materials-17-05825" class="html-bibr">128</a>].</p>
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<p>Examples of gas sensors using commercially available fibers: (<b>a</b>) Gas sensing performance of RGO-cotton yarn and RGO-polyester yarn exposed to 0.25 ppm and 1.25 ppm of NO<sub>2</sub> at room temperature [<a href="#B129-materials-17-05825" class="html-bibr">129</a>]; (<b>b</b>) Gas sensing performance of RGO-cotton yarn and RGO-cotton yarn with MoS<sub>2</sub> exposed to 0.45 ppm, 2.5 ppm, and 4.5 ppm NO<sub>2</sub> gas at room temperature [<a href="#B130-materials-17-05825" class="html-bibr">130</a>]; (<b>c</b>) Schematic illustration of the fabrication process for RGO-elastic yarn [<a href="#B131-materials-17-05825" class="html-bibr">131</a>]; (<b>d</b>) Schematic illustration of the fabrication process of RGO/nylon-6 [<a href="#B134-materials-17-05825" class="html-bibr">134</a>].</p>
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<p>Examples of gas sensors using commercially available fibers: (<b>a</b>) Gas sensing performance of RGO-cotton yarn and RGO-polyester yarn exposed to 0.25 ppm and 1.25 ppm of NO<sub>2</sub> at room temperature [<a href="#B129-materials-17-05825" class="html-bibr">129</a>]; (<b>b</b>) Gas sensing performance of RGO-cotton yarn and RGO-cotton yarn with MoS<sub>2</sub> exposed to 0.45 ppm, 2.5 ppm, and 4.5 ppm NO<sub>2</sub> gas at room temperature [<a href="#B130-materials-17-05825" class="html-bibr">130</a>]; (<b>c</b>) Schematic illustration of the fabrication process for RGO-elastic yarn [<a href="#B131-materials-17-05825" class="html-bibr">131</a>]; (<b>d</b>) Schematic illustration of the fabrication process of RGO/nylon-6 [<a href="#B134-materials-17-05825" class="html-bibr">134</a>].</p>
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<p>Schematic illustration of the fabrication process for RGO–Co<sub>3</sub>O<sub>4</sub> nanofibers involving electrospinning and calcination process [<a href="#B143-materials-17-05825" class="html-bibr">143</a>].</p>
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<p>Schematic illustration of (<b>a</b>) The preparation of hollow In<sub>2</sub>O<sub>3</sub> nanofibers, N-GQDs, and PANI/N-GQD/In<sub>2</sub>O<sub>3</sub> nanofibers, and (<b>b</b>) nanofiber sensor fabrication [<a href="#B147-materials-17-05825" class="html-bibr">147</a>].</p>
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<p>Schematic representation of RGO-In<sub>2</sub>O<sub>3</sub> gas sensing mechanism, depicting depletion layer in air (<b>i</b>) and in NH<sub>3</sub> gas (<b>ii</b>) [<a href="#B150-materials-17-05825" class="html-bibr">150</a>].</p>
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<p>(<b>a</b>) Schematic illustration of MXene/GO via wet-spinning; (<b>b</b>) Selectivity of RGO/Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> MXene to NH<sub>3</sub> in comparison to other gases [<a href="#B153-materials-17-05825" class="html-bibr">153</a>].</p>
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<p>(<b>a</b>) Frequency shifts of G-COOH/PS QCM sensors upon exposure to increasing NH<sub>3</sub> concentrations [<a href="#B158-materials-17-05825" class="html-bibr">158</a>]; (<b>b</b>) Frequency shifts of CA/PEI/GO QCM sensors upon exposure to increasing NH<sub>3</sub> concentrations [<a href="#B162-materials-17-05825" class="html-bibr">162</a>].</p>
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<p>Schematic illustration of the preparation of RGO-ZnO nanofiber sensors [<a href="#B176-materials-17-05825" class="html-bibr">176</a>].</p>
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<p>Gas sensor on e-skin device: (<b>a</b>) Response of gas sensor to different concentrations of acetone vapor; (<b>b</b>) Response of gas sensor to increasing acetone concentrations; (<b>c</b>) Response and recovery time of gas sensor; (<b>d</b>) sensing stability of device under different bending states in 500 ppm of acetone vapor (each color on the plot represents the response for different bending states) [<a href="#B179-materials-17-05825" class="html-bibr">179</a>].</p>
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<p>Schematic depicting RGO-Cu fiber preparation illustrating the content of Cu in the fiber [<a href="#B180-materials-17-05825" class="html-bibr">180</a>].</p>
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<p>(<b>a</b>) Response of GO-SnO<sub>2</sub> nanofibers (II) and SnO<sub>2</sub> without GO (I); (<b>b</b>) Selectivity of GO-SnO<sub>2</sub> nanofibers (II) and SnO<sub>2</sub> without GO (I) to ethanol gas compared to other gases [<a href="#B182-materials-17-05825" class="html-bibr">182</a>].</p>
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<p>(<b>a</b>) Response of RGO-SnO<sub>2</sub> sensor compared to RGO with other nanocarbons to 100 ppm of formaldehyde as a function of temperature; (<b>b</b>) Response of RGO-SnO<sub>2</sub> sensor containing different RGO concentrations as a function of temperature [<a href="#B186-materials-17-05825" class="html-bibr">186</a>].</p>
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<p>Schematic illustration of the preparation of RGO-SnO<sub>2</sub> nanofiber composite [<a href="#B193-materials-17-05825" class="html-bibr">193</a>].</p>
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<p>Schematic illustration of gas sensing mechanism of RGO/(Pt or Pd)/SnO<sub>2</sub> (the change in the potential barrier is presented by the black and red curves) [<a href="#B201-materials-17-05825" class="html-bibr">201</a>].</p>
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<p>Schematic illustration of the synthesis of RGO/(Au or Pd)/ZnO [<a href="#B206-materials-17-05825" class="html-bibr">206</a>].</p>
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<p>(<b>a</b>) Schematic illustrating the gas sensing mechanism of RGO-MoS<sub>2</sub> composite fiber to (<b>a</b>) NO<sub>2</sub> and (<b>b</b>) NH<sub>3</sub> gas [<a href="#B212-materials-17-05825" class="html-bibr">212</a>].</p>
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<p>(<b>a</b>) Schematic illustration of wet-spinning of GO fiber and fiber sensor; (<b>b</b>) Schematic illustrating the sensing mechanism of RGO-ZnO fiber [<a href="#B215-materials-17-05825" class="html-bibr">215</a>].</p>
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20 pages, 8373 KiB  
Article
Performance of Environmentally Friendly Concrete Containing Fly-Ash and Waste Face Mask Fibers
by Adnan Nawaz, Ameer Murad Khan, Amorntep Jirasakjamroonsri, Panumas Saingam, Ali Ejaz, Qudeer Hussain, Hisham Mohamad and Phromphat Thansirichaisree
Sustainability 2024, 16(23), 10385; https://doi.org/10.3390/su162310385 - 27 Nov 2024
Viewed by 264
Abstract
This work was carried out to explore the potential use of used face masks in concrete to develop sustainable green concrete. In this experimental study, used face masks were cut up, removing the ear stripes and internal nose steel wire, to prepare elongated [...] Read more.
This work was carried out to explore the potential use of used face masks in concrete to develop sustainable green concrete. In this experimental study, used face masks were cut up, removing the ear stripes and internal nose steel wire, to prepare elongated fibers. These fibers were incorporated in cement fly ash mixtures as an additive to determine the response of M20-grade concrete. The Class F fly ash (FA) was employed as a fractional substitute of cement up to 25% by weight, whereas the addition of face masks occurred at 0%, 0.125%, and 0.25% by volume of concrete. The testing scheme focused on the mechanical and durability characteristics of the cement FA mixtures carried out after 3, 28, and 60 days of curing. The inclusion of FA and face mask fibers reduced the density of concrete specimens. The compressive, splitting tensile, and flexural strengths of mixes were also reduced at an early age; however, the strength characteristics improved at later ages, compared to the control mix. The combination of both materials in concrete mixtures resulted in lower water absorption, lower bulk water sorption, and lower mass loss values against acid attack at later ages. Similarly, the electrical resistance of concrete substantially enhanced by increasing the percentage of both materials. The experimental results demonstrated that processed face masks can be utilized in cement fly ash mixes without significantly compromising the resultant concrete characteristics. Full article
(This article belongs to the Special Issue Sustainable Approaches for Developing Concrete and Mortar)
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<p>(<b>a</b>) Face masks and (<b>b</b>) face mask fibers.</p>
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<p>Dry density of concrete mixtures after 60 days.</p>
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<p>Three-dimensional surface diagram of dry density of concrete mixes after 60 days.</p>
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<p>Compressive strength results of mixes at different times.</p>
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<p>Relative compressive strength of mixtures.</p>
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<p>Three-dimensional response surface diagram of compressive strength at 28 days.</p>
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<p>Splitting tensile strength findings of mixtures at different times.</p>
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<p>Relative splitting tensile strength of mixtures.</p>
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<p>Three-dimensional response surface diagram of splitting tensile strength at 28 days.</p>
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<p>Flexural strength results of mixes at different ages.</p>
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<p>Relative flexural strength of mixes.</p>
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<p>Three-dimensional response surface diagram of flexural strength at 28 days.</p>
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<p>Ultimate failure modes (<b>a</b>) compression, (<b>b</b>) flexure, and (<b>c</b>) splitting.</p>
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<p>Water absorption results of mixes at 60 days.</p>
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<p>Three-dimensional response surface diagram of water absorption of mixes.</p>
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<p>Variation in bulk water sorption of mixes.</p>
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<p>Three-dimensional response surface diagram of bulk sorption of mixes.</p>
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<p>Mass loss results of mixes due to acid attack.</p>
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<p>Three-dimensional response surface diagram of mass loss of mixes at 28 days.</p>
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<p>Residual compressive strength of tested specimens after acid attack.</p>
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<p>Electrical resistivity results of concrete mixes at 60 days.</p>
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<p>Three-dimensional response surface illustration of electrical resistivity of mixes at 60 days.</p>
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<p>SEM results of control concrete (C100F0M0).</p>
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<p>SEM results of FA concrete sample (C87.5F12.5M0).</p>
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<p>SEM results of FA concrete (C75F25M0).</p>
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23 pages, 16556 KiB  
Article
Physical Characterization of Ecological Briquettes Based on Vertisols and Sorghum Bicolor CS54 Fibers
by Abba Falama, Maxime Dawoua Kaoutoing, Souaibou, Ruben Zieba Falama, Virgil Dumbrava and Danwé Raidandi
Sustainability 2024, 16(23), 10383; https://doi.org/10.3390/su162310383 - 27 Nov 2024
Viewed by 235
Abstract
The aim of this work is to perform the physical characterization of ecological briquettes based on vertisols and fibers of Sorghum bicolor CS54 from the city of Maroua located in the Far North of Cameroon, a country of Sub-Saharan Africa. Three sites of [...] Read more.
The aim of this work is to perform the physical characterization of ecological briquettes based on vertisols and fibers of Sorghum bicolor CS54 from the city of Maroua located in the Far North of Cameroon, a country of Sub-Saharan Africa. Three sites of study have been identified and investigated, namely ZL (Zokok Laddeo), Ngassa (NG), and KG (Kongola). Different percentages of added plant fibers have been realized, including 0%; 2%; 6%; and 8% of fiber additions for each site considered. The experimental tests have revealed that the plasticity of clays is between 16.56% and 25.96%; it is higher in the Zokok Laddéo site (25.96%); and it is between 16.56 and 23.78% for Ngassa and Kongola. The main aggregates observed in the three sites are gravel, which varies between 1.90% and 16.12%, sand between 4.99 and 53.12%, silt, which varies between 2.30 and 36.10%, and clay which fluctuates between 20 and 38.77%. The coefficient of resistance to abrasion varies between 7.19% and 24.35 for the three sites. The highest rates are those of the samples from the Ngassa site (24.35%). The linear shrinkage of the samples varies between 2.9 and 13.04%. The apparent density of the briquettes are between 1587.30 kg/m3 and 2138.13 kg/m3; they are higher for the sites of Zokok Laddéo and Ngassa. The overall coefficient of the capillary rise value is between 0.42% and 16.85%. The interval variation in the obtained results for the different parameters are for most cases and depending on the sites studied in accordance with the defined international standards. These results have proven that the addition of bicolor Sorghum fibers CS54 in vertisols could improve the performance of constructions based on local and eco-friendly materials. Full article
(This article belongs to the Special Issue Green Construction Materials and Sustainability)
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<p>Location of the study area (extracted from North Cameroon Soil Map at 1:100,000, Yaoundé, ORSTOM).</p>
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<p>Location of the sampling areas.</p>
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<p>(<b>a</b>) First profile of used vertisols; (<b>b</b>) second profile of used vertisols.</p>
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<p>(<b>a</b>) Pre-cut fibers; (<b>b</b>) fibers split to 3 mm size.</p>
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<p>Clay material pretreatment stage.</p>
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<p>Pretreatment stage of plant material.</p>
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<p>Capillary process.</p>
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<p>Abrasion test process. 22 cm = Sample length; 2.5 cm = width of wire brush; 3 kg = Tare weight resting on brush for support; 2.8 cm = Height between sample friction surface and brush handle; BTC CNCS = Raw earth brick compressed earth block; 14 cm = lenght of metal part of brush; 4 cm = height of the BTC.</p>
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<p>Experimental briquettes subjected to the linear shrinkage test.</p>
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<p>Particle size curves of the samples studied.</p>
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<p>Reference abrasion coefficient curve.</p>
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<p>Abrasion coefficient curve for 2% addition of plant fibers.</p>
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<p>Abrasion coefficient curve for 6% addition of plant fibers.</p>
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<p>Abrasion coefficient curve for 8% addition of plant fibers.</p>
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<p>An illustration of linear shrinkage as a function of length.</p>
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<p>Linear shrinkage coefficient during drying of experimental briquettes.</p>
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<p>Histograms of capillary rise in samples.</p>
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<p>Apparent densities of experimental briquettes from different sites.</p>
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28 pages, 9817 KiB  
Article
Evaluating the Thermal Shock Resistance of SiC-C/CA Composites Through the Cohesive Finite Element Method and Machine Learning
by Qiping Deng, Yu Xiong, Zirui Du, Jinping Cui, Cheng Peng, Zhiyong Luo, Jinli Xie, Hailong Qin, Zhimin Sun, Qingfeng Zeng and Kang Guan
Appl. Sci. 2024, 14(23), 11025; https://doi.org/10.3390/app142311025 - 27 Nov 2024
Viewed by 232
Abstract
Silicon carbide-coated carbon fiber-reinforced carbon aerogel (SiC-C/CA) composites are ideal for high-temperature applications due to their ability to endure rapid temperature changes without losing structural integrity. However, assessing and optimizing the Thermal Shock Resistance (TSR) of these composites is challenging due to the [...] Read more.
Silicon carbide-coated carbon fiber-reinforced carbon aerogel (SiC-C/CA) composites are ideal for high-temperature applications due to their ability to endure rapid temperature changes without losing structural integrity. However, assessing and optimizing the Thermal Shock Resistance (TSR) of these composites is challenging due to the complexities in measuring thermal and mechanical responses accurately under rapid fluctuations. Herein, we introduce a novel approach combining the cohesive finite element method (CFEM) with machine learning (ML) to address these challenges. The CFEM simulates crack initiation and propagation and captures mechanical behavior under thermal stress, while ML predicts TSR using simulation datasets, reducing the need for empirical trial-and-error processes. Our method achieves a prediction error for coating residual stress within 15.70% to 24.11% before and after thermal shock tests. Additionally, the ML model, developed to predict the average stiffness degradation factor of the SiC coating after three thermal shock cycles, achieves a coefficient of determination (R2) of 0.9171. This combined approach significantly improves the accuracy and efficiency of TSR assessment and can be extended to other coating materials, accelerating the development of high-temperature-resistant materials with optimized TSR for industrial applications. Full article
(This article belongs to the Special Issue Surface Engineering and Advanced Coatings)
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<p>Microstructure and element distribution of the cross-section of the SiC coating.</p>
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<p>SEM images of different regions of the sample including the surface layer, transition layer, and substrate.</p>
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<p>The thermal shock test of the coating samples.</p>
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<p>(<b>a</b>) Thermal shock model; (<b>b</b>) flowchart of sequential thermo-mechanical coupling simulation; (<b>c</b>) cohesive zone model.</p>
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<p>(<b>a</b>) Thermal shock model; (<b>b</b>) flowchart of sequential thermo-mechanical coupling simulation; (<b>c</b>) cohesive zone model.</p>
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<p>(<b>a</b>) FIB-SEM analysis of porous material; RVE models for the porous transition layer with porosity of (<b>b</b>) 0.4 and (<b>c</b>) 0.2.</p>
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<p>(<b>a</b>) Effective Young’s modulus versus porosity [<a href="#B31-applsci-14-11025" class="html-bibr">31</a>,<a href="#B33-applsci-14-11025" class="html-bibr">33</a>,<a href="#B34-applsci-14-11025" class="html-bibr">34</a>,<a href="#B36-applsci-14-11025" class="html-bibr">36</a>,<a href="#B41-applsci-14-11025" class="html-bibr">41</a>], (<b>b</b>) effective Poisson’s ratio versus porosity [<a href="#B36-applsci-14-11025" class="html-bibr">36</a>,<a href="#B37-applsci-14-11025" class="html-bibr">37</a>,<a href="#B38-applsci-14-11025" class="html-bibr">38</a>,<a href="#B42-applsci-14-11025" class="html-bibr">42</a>], (<b>c</b>) effective thermal conductivity versus porosity [<a href="#B39-applsci-14-11025" class="html-bibr">39</a>,<a href="#B43-applsci-14-11025" class="html-bibr">43</a>,<a href="#B44-applsci-14-11025" class="html-bibr">44</a>,<a href="#B45-applsci-14-11025" class="html-bibr">45</a>,<a href="#B46-applsci-14-11025" class="html-bibr">46</a>,<a href="#B47-applsci-14-11025" class="html-bibr">47</a>,<a href="#B48-applsci-14-11025" class="html-bibr">48</a>,<a href="#B49-applsci-14-11025" class="html-bibr">49</a>,<a href="#B50-applsci-14-11025" class="html-bibr">50</a>,<a href="#B51-applsci-14-11025" class="html-bibr">51</a>], and (<b>d</b>) normalized tensile/flexural/compressive strength with porosity [<a href="#B40-applsci-14-11025" class="html-bibr">40</a>,<a href="#B52-applsci-14-11025" class="html-bibr">52</a>,<a href="#B53-applsci-14-11025" class="html-bibr">53</a>,<a href="#B54-applsci-14-11025" class="html-bibr">54</a>,<a href="#B55-applsci-14-11025" class="html-bibr">55</a>,<a href="#B56-applsci-14-11025" class="html-bibr">56</a>].</p>
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<p>Macroscopic morphology of the sample: (<b>a</b>) before the thermal shock test (<b>b</b>) after the first thermal shock test; (<b>c</b>,<b>d</b>) SEM images on the surface and (<b>e</b>,<b>f</b>) SEM images on the cross-sectional surface.</p>
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<p>Residual stress contour map: (<b>a</b>) preparation of residual stress and (<b>b</b>) residual stress after the first thermal shock.</p>
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<p>Damage maps for the A<sub>1</sub>B<sub>3</sub>C<sub>3</sub> model: (<b>a</b>) after the first thermal shock, (<b>b</b>) after the second thermal shock, and (<b>c</b>) after the third thermal shock.</p>
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<p>Stress nephograms for the A<sub>1</sub>B<sub>3</sub>C<sub>3</sub> model (unit: 10<sup>3</sup> GPa): (<b>a</b>) after the first thermal shock, (<b>b</b>) after the second thermal shock, and (<b>c</b>) after the third thermal shock.</p>
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<p>Damage patterns of the original structural configuration: (<b>a</b>) after the first thermal shock, (<b>b</b>) after the second thermal shock, and (<b>c</b>) after the third thermal shock.</p>
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<p>Stress nephograms of the original structural configuration: (<b>a</b>) after the first thermal shock, (<b>b</b>) after the second thermal shock, and (<b>c</b>) after the third thermal shock.</p>
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<p>Performance of machine learning models with the optimal hyperparameter settings on the test data: (<b>a</b>) MSE, (<b>b</b>) MAE, and (<b>c</b>) R<sup>2</sup>.</p>
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<p>Performance of machine learning models with the optimal hyperparameter settings on the test data: (<b>a</b>) MSE, (<b>b</b>) MAE, and (<b>c</b>) R<sup>2</sup>.</p>
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<p>Prediction results using XGBoost regression. The training and testing sets are represented by blue dots and red squares, respectively.</p>
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<p>(<b>a</b>) Feature importance ranking for the target output; (<b>b</b>) SHAP values of each feature for each sample based on XGBoost regression.</p>
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