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11 pages, 7935 KiB  
Article
Characterization of Invar Syntactic Foams Obtained by Spark Plasma Sintering
by Argentina Niculina Sechel, Călin-Virgiliu Prică, Traian Florin Marinca, Florin Popa, Loredana-Maria Baglaevschi, Gyorgy Thalmaier and Ioan Vida-Simiti
Appl. Sci. 2025, 15(6), 2932; https://doi.org/10.3390/app15062932 (registering DOI) - 8 Mar 2025
Viewed by 18
Abstract
This study presents the synthesis of sintered composite foams based on the Invar alloy (64Fe-36Ni), using hollow spherical particles from a nickel superalloy (NiCrSiB) in order to generate porosity. The Invar powder was obtained by mechanical alloying (MA), and the NiCrSiB hollow spherical [...] Read more.
This study presents the synthesis of sintered composite foams based on the Invar alloy (64Fe-36Ni), using hollow spherical particles from a nickel superalloy (NiCrSiB) in order to generate porosity. The Invar powder was obtained by mechanical alloying (MA), and the NiCrSiB hollow spherical particles were incorporated into the composite at 20 vol %. The sintering was realized using the spark plasma sintering (SPS) process in an argon atmosphere at 600 °C and 5 MPa, with 10 s holding time. The porous structures were structurally characterized by optical microscopy (OM), scanning electron microscopy (SEM) and X-ray diffraction (XRD). The coefficient of linear thermal expansion (CTE) of the Invar/NiCrSiB syntactic foams was found to be 2.52 × 10−6 °C−1 in the 25–150 °C temperature range and 19.68 × 10−6 °C−1 in the 150–400 °C range. Full article
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Figure 1

Figure 1
<p>Optical images of Invar powder (<b>a</b>) and NiCrSiB superalloy (<b>b</b>).</p>
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<p>Optical images of the wall thickness (g) of some NiCrSiB superalloy particles; (<b>a</b>) g ≅ 6 μm, (<b>b</b>) g ≅ 26 μm, (<b>c</b>) g ≅ 54 μm.</p>
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<p>Photo images of spark plasma sintered Invar/20%NiCrSiB syntactic foam sample.</p>
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<p>SEM images of Invar/20%NiCrSiB composite foam at different magnifications: 35× (<b>a</b>), 100× (<b>b</b>), 1000× (<b>c</b>) and 5000× (<b>d</b>).</p>
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<p>EDX maps of element distributions of Invar/20%NiCrSiB syntactic foam – mixed elements map distribution (<b>a</b>), map of the Fe (<b>b</b>), map of the Ni (<b>c</b>), map of the Cr (<b>d</b>), map of the Si (<b>e</b>), map of the B (<b>f</b>) and map of the C (<b>g</b>).</p>
Full article ">Figure 5 Cont.
<p>EDX maps of element distributions of Invar/20%NiCrSiB syntactic foam – mixed elements map distribution (<b>a</b>), map of the Fe (<b>b</b>), map of the Ni (<b>c</b>), map of the Cr (<b>d</b>), map of the Si (<b>e</b>), map of the B (<b>f</b>) and map of the C (<b>g</b>).</p>
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<p>SEM image and EDX line scan of Invar/20%NiCrSiB sample.</p>
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<p>XRD diffraction patterns of Invar 16 h milled powders (<b>a</b>), NiCrSiB hollow particles (<b>b</b>) and Invar/20%NiCrSBi spark plasma sintered composite foam (<b>c</b>).</p>
Full article ">Figure 8
<p>Elongation variation (Δl) as a function of temperature for syntactic foam Invar/20% NiCrSiB and for Invar [<a href="#B17-applsci-15-02932" class="html-bibr">17</a>].</p>
Full article ">
14 pages, 4489 KiB  
Article
Preparation and Properties of PETG Filament Modified with a Metallic Additive
by Piotr Zmuda Trzebiatowski, Tomasz Królikowski, Agnieszka Ubowska and Katarzyna Wilpiszewska
Materials 2025, 18(6), 1203; https://doi.org/10.3390/ma18061203 - 7 Mar 2025
Viewed by 90
Abstract
The materials used as filaments for additive techniques should exhibit various properties depending on the application and the requirements. The motivation for this study was the need to obtain a filament exhibiting appropriate aesthetic (metal-like) and mechanical properties. Glycol-modified poly(ethylene terephthalate) copolymer (PETG) [...] Read more.
The materials used as filaments for additive techniques should exhibit various properties depending on the application and the requirements. The motivation for this study was the need to obtain a filament exhibiting appropriate aesthetic (metal-like) and mechanical properties. Glycol-modified poly(ethylene terephthalate) copolymer (PETG) and micrometric steel powder were used for composite preparation. Subsequently, the obtained material was used as a filament for 3D printing, i.e., by fused deposition modeling (FDM) technique. The physicochemical properties of the obtained filaments were determined, such as morphology (roughness), moisture sorption ability, thermal properties, and mechanical performance (tensile and compressive strength). Importantly, the metal filler did not modify the thermal properties of the polyester matrix, indicating that the filament containing steel microfiller could be processed using the same parameters as for neat PETG. The thermal stability was slightly enhanced after steel powder addition (for 13 wt.% content, the temperature of 75% weight loss was 466 °C; for comparison, that for the reference sample was 446 °C). The reinforcing effect of steel microfiller was noted based on mechanical performance measurements. The steel particles acted as a stiffening agent; the highest maximal tensile strength was observed for the composite with 3 wt.% steel powder content (ca. 68 MPa). Further increasing the microfiller load resulted in a slight decrease in the value of this parameter. A different trend was reported considering the compressive strength, i.e., the value of this parameter increased with steel content. Based on the obtained results, the new PETG composites could be applied as structural materials. Full article
(This article belongs to the Special Issue 3D-Printed Composite Structures: Design, Properties and Application)
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Figure 1
<p>The tensile strength test specimens.</p>
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<p>The compressive test specimens.</p>
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<p>The LSM images of PETG filaments containing (<b>A</b>) 0 wt.%, (<b>B</b>) 3 wt., (<b>C</b>) 5 wt.%, (<b>D</b>) 8 wt.%, and (<b>E</b>) 13 wt.% steel filler.</p>
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<p>The DSC thermograms of cooling for PETG filaments with various steel filler content.</p>
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<p>TGA curves of PETG filaments with various steel filler content.</p>
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<p>The moisture absorption of PETG filaments with various steel filler contents.</p>
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<p>The stress–strain curves of PETG systems with various steel filler contents.</p>
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<p>The mechanical strength (<b>A</b>) and elastic modulus (<b>B</b>) for PETG systems with various steel filler contents.</p>
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<p>The LSM images of the PETG-13 composite cross-sections (<b>A</b>) before and (<b>B</b>) after the tensile strength test.</p>
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<p>The compressive curves for PETG systems with various steel filler contents.</p>
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<p>Compressive strength of PETG systems with various steel filler contents.</p>
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16 pages, 1777 KiB  
Article
Cloud Point Behavior of Poly(trifluoroethyl methacrylate) in Supercritical CO2–Toluene Mixtures
by James R. Zelaya and Gary C. Tepper
Molecules 2025, 30(6), 1199; https://doi.org/10.3390/molecules30061199 - 7 Mar 2025
Viewed by 139
Abstract
Supercritical CO2 (scCO2) is a versatile solvent for polymer processing; however, many partially fluorinated polymers exhibit limited solubility in neat scCO2. Organic cosolvents such as toluene can enhance polymer–solvent interactions, thereby improving solubility. The cloud point behavior of [...] Read more.
Supercritical CO2 (scCO2) is a versatile solvent for polymer processing; however, many partially fluorinated polymers exhibit limited solubility in neat scCO2. Organic cosolvents such as toluene can enhance polymer–solvent interactions, thereby improving solubility. The cloud point behavior of poly(2,2,2-trifluoroethyl methacrylate) (poly(TFEMA)) at 3 wt% concentration in scCO2–toluene binary mixtures was investigated over a temperature range of 31.5–50 °C and toluene contents of 0–20 wt%. Solvent mixture densities were estimated using the Altuin–Gadetskii–Haar–Gallagher–Kell (AG–HGK) equation of state for CO2 and the Tait equation for toluene. For all compositions, the cloud point pressure was observed to increase linearly with temperature. The cloud point pressure decreased monotonically with increasing toluene concentration and at the highest concentration of 20 wt% was reduced by approximately 40% in comparison to neat scCO2. The addition of toluene lowered the solvent density, but the increase in solvent–solute molecular interactions resulted in the observed decrease in cloud point pressure. Toluene is shown to be an effective cosolvent for dissolving poly(TFEMA) in scCO2, offering a promising approach to lowering operating pressures in fluoropolymer processing. Our results provide valuable phase behavior data for designing scCO2-based extraction, impregnation, and particle formation processes involving poly(TFEMA). Full article
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Figure 1
<p>Chemical structure of poly(TFEMA). The polymer backbone originates from the methacrylate moiety, featuring an ester group linked to a 2,2,2-trifluoroethyl unit, which enhances its hydrophobicity and chemical resistance.</p>
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<p>Chemical structure of toluene, an aromatic hydrocarbon often employed as a cosolvent in scCO<sub>2</sub> due to its moderate polarity and <math display="inline"><semantics> <mi>π</mi> </semantics></math>–<math display="inline"><semantics> <mi>π</mi> </semantics></math> interaction capability, facilitating polymer dissolution.</p>
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<p>Cloud point pressure vs. temperature for 3 wt% poly(TFEMA) in scCO<sub>2</sub> with varying toluene fractions (0–20 wt%). Error bars are within ±1% of reported values.</p>
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<p>Cloud point pressure vs. toluene wt% at five isothermal conditions: 304.65, 308.15, 313.15, 318.15, and 323.15 K.</p>
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<p>Calculated density of scCO<sub>2</sub>–toluene mixtures as a function of temperature at different toluene weight percentages (0–20 wt%).</p>
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<p>Schematic diagram of the experimental setup for cloud point measurements. The system integrates the CO<sub>2</sub> supply, pressure and temperature control, and optical monitoring for accurate detection of cloud point phenomena.</p>
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<p>Camera images through the quartz window of the Phase Monitor showing (<b>A</b>) a fully dissolved (single-phase) polymer solution, (<b>B</b>) the onset of cloud formation (cloud point), and (<b>C</b>) significant phase separation (polymer precipitation).</p>
Full article ">
22 pages, 8618 KiB  
Article
Suitability of Electrodialysis with Monovalent Selective Anion-Exchange Membranes for Fractionation of Aqueous Mixture Containing Reactive Dye and Mineral Salt
by Katarzyna Majewska-Nowak, Arif Eftekhar Ahmed, Martyna Grzegorzek and Karolina Baraniec
Membranes 2025, 15(3), 85; https://doi.org/10.3390/membranes15030085 - 7 Mar 2025
Viewed by 63
Abstract
To fulfil the goals of the circular economy, the treatment of textile wastewater should be focused on the recovery of valuable components. Monovalent anion-selective electrodialysis (MASED) was applied for the separation of reactive dyes from mineral salts. Standard cation-exchange membranes (CM membranes) and [...] Read more.
To fulfil the goals of the circular economy, the treatment of textile wastewater should be focused on the recovery of valuable components. Monovalent anion-selective electrodialysis (MASED) was applied for the separation of reactive dyes from mineral salts. Standard cation-exchange membranes (CM membranes) and monovalent selective anion-exchange membranes (MVA membranes) were used in the electrodialysis (ED) stack. The separation efficiency was evaluated for model solutions of various reactive dyes (varying in molecular weight and chemical reactivity) containing NaCl. In the course of MASED, the mineral salt was successfully removed from the dye solutions with an efficacy of 97.4–99.4%, irrespectively of the composition of the treated solution. The transport of dye molecules through the ion-exchange membranes (IEMs) from diluate to concentrate compartments was irrelevant. Nonetheless, a significant adsorption of dye particles on the membranes was observed. Around 11–40% of the initial dye mass was deposited in the ED stack. Dye adsorption intensity was significantly affected by dye reactivity. This study showed the potential of the MASED process for the separation of the reactive dye from the mineral salt on condition that antifouling membrane properties are improved. The obtained streams (the concentrate rich in mineral salt and the diluate containing the reactive dye) can be reused in the dye-house textile operations; however, some loss of dye mass should be included. Full article
(This article belongs to the Special Issue Research on Electrodialytic Processes)
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Figure 1
<p>Desalination of NaCl solutions by monovalent anion-selective electrodialysis (MASED): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time.</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (50 mg/L): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (100 mg/L): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time; current: 0.3 A (4.70 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) diluate electrical conductivity versus operation time and (<b>b</b>) desalination efficiency versus operation time; current: 0.45 A (7.05 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) dye concentration in diluate versus operation time and (<b>b</b>) dye concentration in concentrate versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (50 mg/L): (<b>a</b>) dye concentration in diluate versus operation time and (<b>b</b>) dye concentration in concentrate versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
Full article ">Figure 9
<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (100 mg/L): (<b>a</b>) dye concentration in diluate versus operation time and (<b>b</b>) dye concentration in concentrate versus operation time; current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Dye retention in diluate compartments for various reactive dyes at variable dye concentration (20, 50, and 100 mg/L); current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Mass of dye deposited on/in PC-MVA membranes for various reactive dyes at variable dye concentration (20, 50, and 100 mg/L); current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
Full article ">Figure 12
<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) dye concentration in diluate versus operation time and (<b>b</b>) dye concentration in concentrate versus operation time; current: 0.3 A (4.7 mA/cm<sup>2</sup>).</p>
Full article ">Figure 13
<p>Desalination of dye–salt mixtures by MASED for various reactive dyes (20 mg/L): (<b>a</b>) dye concentration in diluate versus operation time and (<b>b</b>) dye concentration in concentrate versus operation time; current: 0.45 A (7.05 mA/cm<sup>2</sup>).</p>
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<p>Dye retention in diluate compartments for various reactive dyes at variable NaCl concentration (2, 4, and 6 g NaCl/L); current: 0.15, 0.3, and 0.45 A, respectively.</p>
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<p>Mass of dye deposited on/in the PC-MVA membranes for various reactive dyes at variable NaCl concentration (2, 4, and 6 g NaCl/L); current: 0.15, 0.3, and 0.45 A, respectively.</p>
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<p>Specific electrical energy consumption during desalination of dye–salt mixtures by MASED for various reactive dyes at variable dye concentration (20, 50, and 100 mg/L); current: 0.15 A (2.35 mA/cm<sup>2</sup>).</p>
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<p>Specific electrical energy consumption during desalination of dye–salt mixtures by MASED for various reactive dyes at variable NaCl concentration (2, 4, and 6 g/L); current: 0.15; 0.3 and 0.45 A, respectively.</p>
Full article ">
27 pages, 1056 KiB  
Article
Quantum Mechanical Numerical Model for Interaction of Dark Atom with Atomic Nucleus of Matter
by Timur Bikbaev, Maxim Khlopov and Andrey Mayorov
Physics 2025, 7(1), 8; https://doi.org/10.3390/physics7010008 - 7 Mar 2025
Viewed by 66
Abstract
Within the framework of the XHe hypothesis, the positive results of the DAMA/NaI and DAMA/LIBRA experiments on the direct search for dark matter particles can be explained by the annual modulation of the radiative capture of dark atoms into low-energy bound states with [...] Read more.
Within the framework of the XHe hypothesis, the positive results of the DAMA/NaI and DAMA/LIBRA experiments on the direct search for dark matter particles can be explained by the annual modulation of the radiative capture of dark atoms into low-energy bound states with sodium nuclei. Since this effect is not observed in other underground WIMP (weakly interacting massive particle) search experiments, it is necessary to explain these results by investigating the possibility of the existence of low-energy bound states between dark atoms and the nuclei of matter. Numerical modeling is used to solve this problem, since the study of the XHe–nucleus system is a three-body problem and leaves no possibility of an analytical solution. To understand the key properties and patterns underlying the interaction of dark atoms with the nuclei of baryonic matter, we develop the quantum mechanical description of such an interaction. In the numerical quantum mechanical model presented, takes into account the effects of quantum physics, self-consistent electromagnetic interaction, and nuclear attraction. This approach allows us to obtain a numerical model of the interaction between the dark atom and the nucleus of matter and interpret the results of direct experiments on the underground search for dark matter, within the framework of the dark atom hypothesis. Thus, in this paper, for the first time, steps are taken towards a consistent quantum mechanical description of the interaction of dark atoms, with unshielded nuclear attraction, with the nuclei of atoms of matter. The total effective interaction potential of the OHe–Na system has therefore been restored, the shape of which allows for the preservation of the integrity and stability of the dark atom, which is an essential requirement for confirming the validity of the OHe hypothesis. Full article
(This article belongs to the Special Issue Beyond the Standard Models of Physics and Cosmology: 2nd Edition)
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Figure 1
<p>Hypothetical qualitative form of the effective interaction potential of XHe dark atom with the nucleus of atom of matter [<a href="#B1-physics-07-00008" class="html-bibr">1</a>]. See text for details.</p>
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<p>The eigenvalues of the helium nucleus Hamiltonian, corresponding to the first three energy levels, in the OHe dark atom potential (red solid line), along with the squared modulus of the wave functions associated with these energy levels (blue solid line). The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>Interaction potentials in the OHe–Na system for fixed <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math>, including the Coulomb interaction (green dotted line) and nuclear interaction (black dotted line) between the helium nucleus and the sodium nucleus, as well as the Coulomb potential between the helium nucleus and the <math display="inline"><semantics> <msup> <mi mathvariant="normal">O</mi> <mrow> <mo>−</mo> <mo>−</mo> </mrow> </msup> </semantics></math> particle (blue dotted line). The combined total interaction potential experienced by the helium nucleus is represented by the red dotted line. The red circle shows the radius of the helium. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The dependence of the helium ground-state energy in the polarized OHe (blue stars) on the radius vector of the sodium nucleus. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The red solid line represents the total interaction potential of helium in the OHe–Na system for a fixed position of the sodium nucleus, <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math>. The blue solid line illustrates the squared modulus of the helium ground-state wave function within the polarized dark atom at the same fixed <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math>. Black circles denote the intersection points between the graph of the total helium potential and the squared modulus of its wave function in the ground state. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The relationship between the dipole moment of the polarized OHe (blue stars) and the radius vector of the external sodium nucleus. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The dependence of the dipole moment of the polarized OHe (blue stars) on the radius vector of the sodium nucleus at the moment when the dark atom undergoes repolarization. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The squared modulus of the wave functions (blue solid line) for specific energy levels of helium in its ground state within the total interaction potential of the OHe–Na system (red solid line). These lines correspond to the particular positions of the sodium nucleus <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math>, marking the onset of the dark atom’s repolarization. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The squared modulus of the wave functions (blue solid line) for certain ground-state energy levels of helium within the total potential of the OHe–Na system (red solid line). These are associated with the positions of the sodium nucleus <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math> at the stage when helium begins tunneling with high probability from the repolarized dark atom into the sodium nucleus. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>Various interaction potentials as functions of the distance between the helium nucleus, located within the Bohr orbit of the OHe, and the sodium: the nuclear potential in the Woods–Saxon form (black dotted line, overlapped by the blue dotted line), <math display="inline"><semantics> <msubsup> <mi>U</mi> <mi>XHe</mi> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> (green dotted line), the Stark potential (red dotted line, overlapped by the blue dotted line), and the total effective interaction potential of OHe with the sodium (blue dotted line). The black circle highlights the addition amount of the radii of the helium and sodium nuclei. The radius vector of helium is set to <math display="inline"><semantics> <mrow> <mi>r</mi> <mo>=</mo> <mo>|</mo> <mn>1.1</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>12</mn> </mrow> </msup> <mrow> <mspace width="3.33333pt"/> <mi>cm</mi> <mo>|</mo> </mrow> </mrow> </semantics></math>. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
Full article ">Figure 11
<p>Various interaction potentials as functions of the separation between the helium and the sodium: the Woods–Saxon nuclear potential (black dotted line), the <math display="inline"><semantics> <msubsup> <mi>U</mi> <mi>XHe</mi> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> potential (green dotted line), the Stark potential (red dotted line), and the total effective interaction potential for the OHe–Na system (blue dotted line). The radius vector of He was set equal to <math display="inline"><semantics> <mrow> <mi>r</mi> <mo>=</mo> <mo>|</mo> <mn>1.1</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>12</mn> </mrow> </msup> <mrow> <mspace width="3.33333pt"/> <mi>cm</mi> <mo>|</mo> </mrow> </mrow> </semantics></math> during the phase of repolarization of the OHe. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
Full article ">Figure 12
<p>Various interaction potentials as functions of the separation between the helium and the sodium: the Woods–Saxon nuclear potential (black dotted line, overlapped by the green dotted line), the <math display="inline"><semantics> <msubsup> <mi>U</mi> <mi>XHe</mi> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> potential (green dotted line), the Stark potential (red dotted line, overlapped by the blue dotted line), and the total effective interaction potential between OHe and the sodium (blue dotted line). The radius vector of helium was set equal to <math display="inline"><semantics> <mrow> <mi>r</mi> <mo>=</mo> <mo>|</mo> <mn>2.5</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>12</mn> </mrow> </msup> <mrow> <mspace width="3.33333pt"/> <mi>cm</mi> <mo>|</mo> </mrow> </mrow> </semantics></math>. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>Dependence of various potentials on the separation between the helium and the sodium: the Woods–Saxon nuclear potential (black dotted line, overlapped by the green dotted line), <math display="inline"><semantics> <msubsup> <mi>U</mi> <mi>XHe</mi> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> (green dotted line), the Stark potential (red dotted line, overlapped by the blue dotted line), and the total effective interaction potential (blue dotted line). The radius vector of helium was set equal to <math display="inline"><semantics> <mrow> <mi>r</mi> <mo>=</mo> <mo>|</mo> <mn>2.5</mn> <mo>×</mo> <msup> <mn>10</mn> <mrow> <mo>−</mo> <mn>12</mn> </mrow> </msup> <mrow> <mspace width="3.33333pt"/> <mi>cm</mi> <mo>|</mo> </mrow> </mrow> </semantics></math> during the phase when the dark atom undergoes repolarization. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>The interaction potentials in the OHe–Na system for specific fixed value of <math display="inline"><semantics> <msub> <mover accent="true"> <mi>R</mi> <mo>→</mo> </mover> <mi>OA</mi> </msub> </semantics></math>, including the Coulomb interaction potential (green dotted line), nuclear interaction potential (black dotted line), and the centrifugal interaction potential (magenta solid line) between the He and the Na nucleus. Additionally, the Coulomb interaction potential between He and the <math display="inline"><semantics> <msup> <mi mathvariant="normal">O</mi> <mrow> <mo>−</mo> <mo>−</mo> </mrow> </msup> </semantics></math> is shown by blue dashed line, while the total interaction potential experienced by the He is represented by the red dotted line. The black circle shows the radius of the helium. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>Various interaction potentials relevant to the OHe–Na system: the Woods–Saxon nuclear interaction potential (black dotted line), the <math display="inline"><semantics> <msubsup> <mi>U</mi> <mrow> <mi>XHe</mi> </mrow> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> interaction potential (yellow dotted line), the Stark interaction potential (red dotted line), the centrifugal interaction potential (green dotted line), and the total effective interaction potential (blue dotted line). Potentials shown as a function of the separation distance between He in OHe and Na. The case corresponds to <math display="inline"><semantics> <mrow> <msub> <mover accent="true"> <mi>J</mi> <mo>→</mo> </mover> <mrow> <mi>OHe</mi> <mo>−</mo> <mi>Na</mi> </mrow> </msub> <mo>=</mo> <mover accent="true"> <mrow> <mn>3</mn> <mo>/</mo> <mn>2</mn> </mrow> <mo>→</mo> </mover> </mrow> </semantics></math>. See text for details. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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<p>Various interaction potentials within the OHe–Na system, presented as functions of the separation distance between the He in OHe and Na: the Woods–Saxon nuclear interaction potential (black dotted line), the <math display="inline"><semantics> <msubsup> <mi>U</mi> <mrow> <mi>XHe</mi> </mrow> <mi mathvariant="normal">e</mi> </msubsup> </semantics></math> interaction potential (yellow dotted line), the Stark interaction potential (red dotted line), the centrifugal interaction potential (green dotted line), and the total effective interaction potential (blue dotted line). The case corresponds to <math display="inline"><semantics> <mrow> <msub> <mover accent="true"> <mi>J</mi> <mo>→</mo> </mover> <mrow> <mi>OHe</mi> <mo>−</mo> <mi>Na</mi> </mrow> </msub> <mo>=</mo> <mover accent="true"> <mn>3</mn> <mo>→</mo> </mover> </mrow> </semantics></math>. The results of the paper [<a href="#B16-physics-07-00008" class="html-bibr">16</a>] were used in the calculations.</p>
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16 pages, 5538 KiB  
Article
Magnetic Coal Gasification Slag/Graphite Phase Carbon Nitride Composites for Photocatalytic Degradation of Tetracycline
by Yue Yin, Tingan Yao, Guohui Dong and Chuanyi Wang
Processes 2025, 13(3), 770; https://doi.org/10.3390/pr13030770 - 7 Mar 2025
Viewed by 187
Abstract
Graphite-phase carbon nitride (CN) has the advantages of high stability, non-toxicity, and harmlessness in degrading antibiotic pollutants in water. How to achieve the reduction of its electron-hole complexation efficiency as well as the improvement of its recyclability, while at the same time ensuring [...] Read more.
Graphite-phase carbon nitride (CN) has the advantages of high stability, non-toxicity, and harmlessness in degrading antibiotic pollutants in water. How to achieve the reduction of its electron-hole complexation efficiency as well as the improvement of its recyclability, while at the same time ensuring these advantages, is the focus of this paper. In this study, modified magnetic particles selected from coal gasification slag were used as carriers, which were compounded with CN and then subjected to a simple roasting process to obtain composite magnetic photocatalysts (MCN) with different ratios. The introduction of porous magnetic carriers increased the specific surface area of MCN, provided more active sites, and effectively improved the migration ability and redox capacity of CN carriers. Among them, 50% MCN showed excellent photodegradation performance, and the removal rate of tetracycline reached 82% within 60 min, which was much higher than that of CN. 50% MCN has a saturated magnetisation intensity of 1.55 emu·g−1, which can be regenerated after recycling using a magnetic field, and the degradation efficiency of tetracycline is still more than 70% after five cycles, indicating that 50% MCN has good stability. This work demonstrates that magnetic gasification slag as a modified carrier can effectively promote the separation of photogenerated electron-hole pairs of graphite-phase carbon nitride, which provides a reference for the resourceful utilisation of coal gasification slag, as well as for the construction of g-C3N4-based photocatalysts with highly efficient and stable photodegradation activity. This work exemplifies how waste-derived materials can advance photocatalyst design, addressing both efficiency and sustainability challenges in water treatment. Full article
(This article belongs to the Section Environmental and Green Processes)
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<p>Preparation process diagram of MCN.</p>
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<p>(<b>a</b>) Appearance of the five samples; X-ray diffraction spectra of (<b>b</b>) Coal gasification residue and (<b>c</b>) MAGM.</p>
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<p>(<b>a</b>) X-ray diffraction spectra of magnetic composite photocatalytic materials; (<b>b</b>) FT-IR spectroscopy of magnetic composite photocatalytic materials; (<b>c</b>) Hysteresis loops for MAGM and 50% MCN; (<b>d</b>) Schematic diagram of CN and MAGM composite process.</p>
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<p>CN, MAGM and 50% MCN thermogravimetric (<b>a</b>) and DTG (<b>b</b>); N<sub>2</sub> adsorption-desorption curve (<b>c</b>) and pore distribution (<b>d</b>) of magnetic composite photocatalytic materials.</p>
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<p>Scanning electron micrographs of magnetic composite photocatalytic materials: (<b>a</b>,<b>d</b>) CN; (<b>b</b>,<b>e</b>) MAGM; (<b>c</b>,<b>f</b>) 50% MCN.</p>
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<p>(<b>a</b>) Dark adsorption of TC by the magnetic composite photocatalytic material; (<b>b</b>) Degradation of TC under light irradiation; (<b>c</b>) Standard curve of TC; (<b>d</b>) First-order kinetic fitting of the photocatalytic degradation.</p>
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<p>(<b>a</b>) UV-Vis Diffuse Reflectance Spectroscopy (DRS); (<b>b</b>) Bandgaps of different samples; (<b>c</b>) Photoluminescence (PL) spectrogram of MAGM; (<b>d</b>) Photoluminescence spectrograms of CN and x MAGM.</p>
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<p>(<b>a</b>) Transient photocurrent responses of CN, 10% MCN, 50% MCN, and 90% MCN; (<b>b</b>) Transient photocurrent response of MAGM; (<b>c</b>) Impedance fitting spectra of CN, MAGM, 10% MCN, 50% MCN, and 90% MCN; (<b>d</b>) Impedance fitting spectra of 50% MCN under light and dark conditions.</p>
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<p>Free Radical Trapping Experiment for TC Degradation by 50% MCN.</p>
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<p>50% MCN cycle five times degradation of TC: (<b>a</b>) dark reaction; (<b>b</b>) illumination; (<b>c</b>) XRD before and after cycling; (<b>d</b>) pre- and post-cycle infrared spectroscopy; (<b>e</b>) Magnetic recovery process after 5 cycles of TC degradation (Recovery time &lt; 30 s).</p>
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21 pages, 10727 KiB  
Article
Co-Combustion of Coal and Biomass: Heating Surface Slagging and Flue Gases
by Andrey Zhuikov, Dmitrii Glushkov, Andrey Pleshko, Irina Grishina and Stanislav Chicherin
Fire 2025, 8(3), 106; https://doi.org/10.3390/fire8030106 - 7 Mar 2025
Viewed by 174
Abstract
An experimental study was carried out on the ignition and combustion processes of particles (100–200 µm in size) of coals of different degrees of metamorphism and biomass, as well as mixtures based on them, under conditions of conductive and convective heating, which correspond [...] Read more.
An experimental study was carried out on the ignition and combustion processes of particles (100–200 µm in size) of coals of different degrees of metamorphism and biomass, as well as mixtures based on them, under conditions of conductive and convective heating, which correspond to the conditions of fuel ignition in boiler furnaces at grates and flaring combustion. The biomass contents in the composition of the coal-based fuel mixtures were 10, 20, and 30 wt.%. Under the conductive (at 700–1000 °C) and convective (at 500–800 °C) heating of fuel particles, ignition delay times were determined using a hardware–software complex for the high-speed video registration of fast processes. The ignition delay times were found to vary from 1 to 12.2 s for conductive heating and from 0.01 to 0.19 s for convective heating. The addition of 10–30 wt.% biomass to coals reduced the ignition delay times of fuel mixtures by up to 70%. An analysis of the flue gas composition during the combustion of solid fuels allowed us to establish the concentrations of the main anthropogenic emissions. The use of biomass as an additive (from 10 to 230 wt.%) to coal reduced NOx and SOx emissions by 19–42% and 24–39%, respectively. The propensity of fuels to cause slagging depending on their component composition was established. The use of up to 30 wt.% of biomass in the mixture composition did not affect the increase in the tendency to cause slagging on heating surfaces in the boiler furnace and did not pose a threat to the layer agglomeration during the layer combustion of the mixtures. Full article
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<p>Schematic diagram of the experimental setup for fuel combustion under conditions of conductive heating.</p>
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<p>A schematic diagram of the experimental setup for fuel combustion under convective heating conditions.</p>
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<p>A schematic diagram of the experimental setup for studying the composition of flue gases during the combustion of fuels.</p>
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<p>SEM images of investigated fuels: (<b>a</b>) lignite particles; (<b>b</b>) bituminous coal particles; (<b>c</b>) biomass particles.</p>
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<p>Video frames of videograms of ignition and combustion of lignite particles (composition Cb) under conditions of conductive heating at <span class="html-italic">T</span><sub>g</sub> = 800 °C.</p>
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<p>Video frames of videograms of ignition and combustion of bituminous coal particles (composition Ch) under conditions of conductive heating at <span class="html-italic">T</span><sub>g</sub> = 800 °C.</p>
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<p>Video frames of videograms of ignition and combustion of biomass particles (composition B) under conditions of conductive heating at <span class="html-italic">T<sub>g</sub></span> = 800 °C.</p>
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<p>Dependences of ignition delay times of coal, biomass, and their mixtures on oxidizer temperature under conductive heating conditions: (<b>a</b>) brown coal (Cb), biomass (B), and their mixtures (CbB-1, CbB-2, and CbB-3); (<b>b</b>) bituminous coal (Ch), biomass (B), and their mixtures (ChB-1, ChB-2, and ChB-3).</p>
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<p>Video frames of videograms of ignition and combustion of lignite particles (composition Cb) under conditions of movement in flow of heated air at <span class="html-italic">T</span><sub>a</sub> = 700 °C (Δ<span class="html-italic">t</span> = 0.01 s): (<b>a</b>) <span class="html-italic">t</span><sub>d</sub> = 0.052 s; (<b>b</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + ∆<span class="html-italic">t</span>; (<b>c</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 2∆<span class="html-italic">t</span>; (<b>d</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 3∆<span class="html-italic">t</span>.</p>
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<p>Video frames of videograms of ignition and combustion of bituminous coal particles (composition Ch) under conditions of motion in flow of heated air at <span class="html-italic">T<sub>a</sub></span> = 700 °C (Δ<span class="html-italic">t</span> = 0.01 s): (<b>a</b>) <span class="html-italic">t</span><sub>d</sub> = 0.095 s; (<b>b</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + ∆<span class="html-italic">t</span>; (<b>c</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 2∆<span class="html-italic">t</span>; (<b>d</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 3∆<span class="html-italic">t</span>.</p>
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<p>Video frames of videograms of ignition and combustion of biomass particles (composition B) under conditions of motion in flow of heated air at <span class="html-italic">T<sub>a</sub></span> = 700 °C (Δ<span class="html-italic">t</span> = 0.01 s): (<b>a</b>) <span class="html-italic">t</span><sub>d</sub> = 0.030 s; (<b>b</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + ∆<span class="html-italic">t</span>; (<b>c</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 2∆<span class="html-italic">t</span>; (<b>d</b>) <span class="html-italic">t</span> = <span class="html-italic">t</span><sub>d</sub> + 3∆<span class="html-italic">t</span>.</p>
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<p>Dependences of ignition delay times of coal, biomass, and their mixtures on oxidant temperature under convective heating conditions: (<b>a</b>) brown coal (Cb), biomass (B), and their mixtures (CbB-1, CbB-2, and CbB-3); (<b>b</b>) bituminous coal (Ch), biomass (B), and their mixtures (ChB-1, ChB-2, and ChB-3).</p>
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<p>Composition of flue gases during combustion of lignite (Cb), biomass (B), and their mixtures (CbB-1, CbB-2, and CbB-3) at 800 °C: (<b>a</b>) CO and CO<sub>2</sub>; (<b>b</b>) NO<sub>x</sub> and SO<sub>x</sub>.</p>
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<p>Composition of flue gases during combustion of bituminous coal (Ch), biomass (B), and their mixtures (CbB-1, CbB-2, and CbB-3) at 800 °C: (<b>a</b>) CO and CO<sub>2</sub>; (<b>b</b>) NO<sub>x</sub> and SO<sub>x</sub>.</p>
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<p>Boiler furnace for layer combustion of solid fuel mixtures: (<b>a</b>) with one fuel bunker; (<b>b</b>) with two fuel bunkers.</p>
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<p>Boiler furnace for flaring combustion of solid fuel mixture: (<b>a</b>) with single common fuel bunker; (<b>b</b>) with two fuel bunkers.</p>
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<p>Flare combustion boiler furnace equipped with down draft nozzle.</p>
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13 pages, 1891 KiB  
Article
Microstructure-Based Magneto-Mechanical Modeling of Magnetorheological Elastomer Composites: A Comparable Analysis of Dipole and Maxwell Methods
by Shengwei Feng and Lizhi Sun
Materials 2025, 18(5), 1187; https://doi.org/10.3390/ma18051187 - 6 Mar 2025
Viewed by 113
Abstract
Magnetorheological elastomers (MREs) are smart composite materials with tunable mechanical properties by ferromagnetic particle interactions. This study applied the microstructure-based dipole and Maxwell methods to evaluate the magneto-mechanical coupling and magnetostrictive responses of MREs, focusing on various particle distributions. The finite element modeling [...] Read more.
Magnetorheological elastomers (MREs) are smart composite materials with tunable mechanical properties by ferromagnetic particle interactions. This study applied the microstructure-based dipole and Maxwell methods to evaluate the magneto-mechanical coupling and magnetostrictive responses of MREs, focusing on various particle distributions. The finite element modeling of representative volume elements with fixed volume fractions revealed that the straight chain microstructure exhibits the most significant magnetostrictive effect due to its low initial shear stiffness and significant magnetic force contributions. For particle separations exceeding three radii, the dipole and Maxwell methods yield consistent results for vertically or horizontally aligned particles. For particle separations greater than three radii, the dipole and Maxwell methods produce consistent results for vertically and horizontally aligned particles. However, discrepancies emerge for angled configurations and complex microstructures, with the largest deviation observed in the hexagonal particle distribution, where the two methods differ by approximately 27%. These findings highlight the importance of selecting appropriate modeling methods for optimizing MRE performance. Since anisotropic MREs with straight-chain alignments are the most widely used, our results confirm that the dipole method offers an efficient alternative to the Maxwell method for simulating these structures. Full article
(This article belongs to the Special Issue Smart Soft Materials: From Design to Applications)
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<p>RVEs of MRE composites with (<b>a</b>) square, (<b>b</b>) hexagonal, and (<b>c</b>) random distributions of particles. The purple color represents the matrix, while the blue color represents the particles.</p>
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<p>Effective shear modulus comparison for RVEs without magnetic field. The black dashed lines and red dashed lines indicate the upper and lower bound estimates given by HSB-L and SCM, respectively.</p>
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<p>Magnetic interaction forces between two particles with (<b>a</b>) vertical and (<b>b</b>) horizontal alignment. The forces are calculated based on particle <span class="html-italic">i</span>, where positive values indicate attraction and negative values indicate repulsion.</p>
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<p>The x and y components of magnetic interaction forces between two particles with different angles (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>F</mi> </mrow> <mrow> <mi>n</mi> <mi>y</mi> </mrow> </msub> </mrow> </semantics></math> and (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>F</mi> </mrow> <mrow> <mi>n</mi> <mi>x</mi> </mrow> </msub> </mrow> </semantics></math>.</p>
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<p>RVEs with various microstructures: (<b>a</b>) square, (<b>b</b>) hexagonal, (<b>c</b>) straight chain, and (<b>d</b>) wavy chain. The purple color represents the matrix, while the blue color represents the particles.</p>
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<p>Comparison of the relative magnetostrictive effect between the dipole method and the Maxwell method for different particle distributions: (<b>a</b>) square, (<b>b</b>) hexagonal, (<b>c</b>) straight chain, and (<b>d</b>) wavy chain.</p>
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16 pages, 3807 KiB  
Article
A Study on the Effect of Conductive Particles on the Performance of Road-Suitable Barium Titanate/Polyvinylidene Fluoride Composite Materials
by Zhenhua Zhao, Rui Li, Chen Zhao and Jianzhong Pei
Materials 2025, 18(5), 1185; https://doi.org/10.3390/ma18051185 - 6 Mar 2025
Viewed by 117
Abstract
The design of piezoelectric roads is one of the future directions of smart roads. In order to ensure the environmentally friendly and long-lasting use of piezoelectric road materials, lead-free piezoelectric ceramics (barium titanate), polymer piezoelectric materials (polyvinylidene fluoride), and conductive particles (conductive carbon [...] Read more.
The design of piezoelectric roads is one of the future directions of smart roads. In order to ensure the environmentally friendly and long-lasting use of piezoelectric road materials, lead-free piezoelectric ceramics (barium titanate), polymer piezoelectric materials (polyvinylidene fluoride), and conductive particles (conductive carbon black and graphene) were used to prepare composite piezoelectric materials. The electrical performance was studied by the conductivity, dielectric properties, and piezoelectric properties of the composite materials. Then, the mechanical properties of the composite material were investigated by load compression tests. Finally, the microstructure of the composite materials was studied. The results showed that as the amount of conductive particles increased, the electrical performance was improved. However, further addition of conductive particles led to a decline in the electrical performance. The addition of conductive particles had a minimal effect on the mechanical properties of composite materials. The composite material met road use requirements. The overall structure of the composite materials was compact, with a clear wrapping effect of the polymer, and good interface compatibility. The addition of conductive carbon black and graphene had no significant impact on the structure of the composite materials. Full article
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<p>The particle size distribution, SEM, and XRD images of BaTiO3 made by hydrothermal synthesis: (<b>a</b>) particle size distribution; (<b>b</b>) SEM; (<b>c</b>) XRD.</p>
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<p>The preparation method of BaTiO<sub>3</sub>/PVDF composite materials.</p>
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<p>The electrical performance of BaTiO<sub>3</sub>/PVDF composite materials: (<b>a</b>) dielectric properties; (<b>b</b>) piezoelectric properties.</p>
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<p>The influence of conductive particles on the electrical conductivity of three-phase composite materials: (<b>a</b>) conductive carbon black; (<b>b</b>) graphene.</p>
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<p>The influence of conductive particles on the dielectric properties of three-phase composite materials: (<b>a</b>) conductive carbon black; (<b>b</b>) graphene.</p>
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<p>The frequency-dependent dielectric properties of BaTiO<sub>3</sub>/PVDF/conductive carbon black composite materials: (<b>a</b>) relative dielectric constant; (<b>b</b>) dielectric loss.</p>
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<p>The frequency-dependent dielectric properties of BaTiO<sub>3</sub>/PVDF/graphene composite materials: (<b>a</b>) relative dielectric constant; (<b>b</b>) dielectric loss.</p>
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<p>The influence of conductive particles on the piezoelectric properties of three-phase composite materials: (<b>a</b>) conductive carbon black; (<b>b</b>) graphene.</p>
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<p>The influence of conductive particles on the mechanical performance of three-phase composite materials.</p>
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<p>The microscopic morphology of three-phase composite materials: (<b>a</b>) BaTiO<sub>3</sub>/PVDF composite materials; (<b>b</b>) 1.2% conductive carbon black in BaTiO<sub>3</sub>/PVDF composite materials; (<b>c</b>) 0.5% graphene in BaTiO<sub>3</sub>/PVDF composite materials.</p>
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16 pages, 7306 KiB  
Article
Fabrication of Cu/SiC Surface Composite via Thermo-Mechanical Process (Friction Stir Processing) for Heat Sink Application
by Harikishor Kumar, Abhishek Agarwal, Michel Kalenga Wa Kalenga, Rabindra Prasad, Parshant Kumar, L. Aslesha Chilakamarri and Balram Yelamasetti
Materials 2025, 18(5), 1179; https://doi.org/10.3390/ma18051179 - 6 Mar 2025
Viewed by 154
Abstract
For the busting of heat, generated in electronic packages, relevant materials need to be developed. Metal matrix composites may be considered as an option to tailor the properties of a material (Cu) by incorporating an additional phase (SiC) for fulfilling the requirements of [...] Read more.
For the busting of heat, generated in electronic packages, relevant materials need to be developed. Metal matrix composites may be considered as an option to tailor the properties of a material (Cu) by incorporating an additional phase (SiC) for fulfilling the requirements of thermal management systems. The composite (Cu/SiC) was manufactured by friction stir processing. For good interfacial strength, the biggest challenge in the fabrication of Cu/SiC composite was to abolish the reaction between Cu and SiC. Being solid in nature, the process (friction stir processing) does not allow temperature to reach the interfacial interaction. Scanning electron microscopy, electron backscattered diffraction, and optical microscopy were used to characterise the composite for microstructural features (particle dispersion, phases present). To confirm the presence of reinforcement, EDS analysis was also performed on the composite. Results indicated the presence of Cu and SiC phases in the stir zone (SZ) with uniform and homogeneous separation of reinforcements. The composite displayed higher hardness, tensile strength, and wear resistance in comparison to unprocessed copper. However, ductility decreased due to high hardness in the composite. Full article
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<p>SEM micrograph of the reinforcement (SiC).</p>
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<p>Schematic diagrams for composite fabrication via FSP. (<b>a</b>) The plate of known dimension (<b>b</b>) Groove making on the surface of the plate (<b>c</b>) Filling of particles in the groove (<b>d</b>) Closing of the groove with a pin-less tool (<b>e</b>) Processing of the plate (<b>f</b>) The tool with a pin used for processing.</p>
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<p>(<b>a</b>) top view of the processed plate (<b>b</b>) cross-sectional macrostructure.</p>
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<p>Microstructure of (<b>a</b>) base copper and (<b>b</b>) the processed plate without reinforcement.</p>
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<p>Optical images of the nugget zone captured (<b>a</b>) at the top of the zone, (<b>b</b>) at the bottom of the zone, (<b>c</b>) at the centre of the zone, and (<b>d</b>) at the interface between reinforced and non-reinforced.</p>
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<p>SEM images of the nugget zone of the composite at different magnifications (<b>a</b>) 500×, (<b>b</b>) 1000× and (<b>c</b>) 2000×.</p>
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<p>EBSD images of (<b>a</b>) base copper and (<b>c</b>) composite and grain size distribution (<b>b</b>,<b>d</b>).</p>
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<p>(<b>a</b>) The SEM image of the processed section of the composite (<b>b</b>–<b>e</b>) the EDS maps of the elements and their distribution.</p>
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<p>Microhardness profile of the composite.</p>
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<p>Stress–strain curve for the composite and base copper.</p>
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<p>The SEM micrograph of fractured surfaces of (<b>a</b>) base copper and (<b>b</b>) the composite.</p>
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<p>The wear rate profile of base copper and the composite.</p>
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<p>SEM morphology of worn-out surfaces of (<b>a</b>) base copper and (<b>b</b>) the composite.</p>
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19 pages, 8848 KiB  
Article
Tribological Behavior and Mechanism of Silane-Bridged h-BN/MoS2 Hybrid Filling Epoxy Solid Lubricant Coatings
by Xiaoxiao Peng, Haiyan Jing, Lan Yu, Zongdeng Wu, Can Su, Ziyu Ji, Junjie Shu, Hua Tang, Mingzhu Xia, Xifeng Xia, Wu Lei and Qingli Hao
Nanomaterials 2025, 15(5), 401; https://doi.org/10.3390/nano15050401 - 6 Mar 2025
Viewed by 136
Abstract
To significantly improve the tribological performance of epoxy resin (EP), a novel h-BN/MoS2 composite was successfully synthesized using spherical MoS2 particles with lamellar self-assembly generated through the calcination method, followed by utilizing the “bridging effect” of a silane coupling agent to [...] Read more.
To significantly improve the tribological performance of epoxy resin (EP), a novel h-BN/MoS2 composite was successfully synthesized using spherical MoS2 particles with lamellar self-assembly generated through the calcination method, followed by utilizing the “bridging effect” of a silane coupling agent to achieve a uniform and vertically oriented decoration of hexagonal boron nitride (h-BN) nanosheets on the MoS2 surface. The chemical composition and microstructure of the h-BN/MoS2 composite were systematically investigated. Furthermore, the enhancement effect of composites with various contents on the frictional properties of epoxy coatings was studied, and the mechanism was elucidated. The results demonstrate that the uniform decoration of h-BN enhances the chemical stability of MoS2 in friction tests, and the MoS2 prevents oxidation and maintains its self-lubricating properties. Consequently, due to the protective effect of h-BN and the synergistic interaction between h-BN and MoS2, the 5 wt % h-BN/MoS2 composite exhibited the best friction and wear resistance when incorporated into EP. Compared to pure EP coatings, its average friction coefficient and specific wear rate (0.026 and 1.5 × 10−6 mm3 N−1 m−1, respectively) were significantly reduced. Specifically, the average friction coefficient decreased by 88% and the specific wear rate decreased by 99%, highlighting the superior performance of the h-BN/MoS2-enhanced epoxy composite coating. Full article
(This article belongs to the Section 2D and Carbon Nanomaterials)
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<p>The schematic diagrams of the preparation processes for (<b>a</b>) KH560-MoS<sub>2</sub>, (<b>b</b>) KH550-BN, and (<b>c</b>) h-BN/MoS<sub>2</sub>.</p>
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<p>(<b>a</b>) XRD patterns of BN, KH550-BN, MoS<sub>2</sub>, KH560-MoS<sub>2</sub>, and h-BN/MoS<sub>2</sub> hybrids, FT-IR spectra of (<b>b</b>) BN, BN-OH, KH550-BN, and (<b>c</b>) MoS<sub>2</sub>, KH560-MoS<sub>2</sub>, and h-BN/MoS<sub>2</sub> hybrids, and (<b>d</b>) Raman spectroscopy of MoS<sub>2</sub> and KH560-MoS<sub>2</sub>.</p>
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<p>(<b>a</b>) Full-range XPS spectra and high-resolution spectra of h-BN/MoS<sub>2</sub> hybrids including (<b>b</b>) B 1s, (<b>c</b>) Mo 3d, (<b>d</b>) C 1s, (<b>e</b>) N 1s, and (<b>f</b>) S 2p.</p>
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<p>(<b>a</b>) TEM images of h-BN/MoS<sub>2</sub> hybrids, (<b>b</b>–<b>e</b>) HRTEM image, and the corresponding SAED patterns of h-BN/MoS<sub>2</sub> hybrids. (<b>f</b>) Elemental mapping of h-BN/MoS<sub>2</sub> hybrids.</p>
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<p>(<b>a</b>,<b>c</b>) The friction coefficients of the samples as a function of sliding time. (<b>b</b>,<b>d</b>) The friction coefficients’ error bar for different samples.</p>
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<p>(<b>a</b>) Wear rates and wear track width of the coatings for different samples. (<b>b</b>) Vickers hardnesses of the coatings with different samples. (<b>c</b>) The long-cycle tribological performance of 5 wt % h-BN/MoS<sub>2</sub>.</p>
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<p>(<b>a</b>,<b>b</b>) TGA and (<b>c</b>,<b>d</b>) DTG curves of pure EP, 5 wt % MoS<sub>2</sub>/EP, and 5 wt % h-BN/MoS<sub>2</sub> /EP under N<sub>2</sub> and air atmospheres.</p>
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<p>Fracture sections for different coatings: (<b>a</b>) EP, (<b>b</b>) 5 wt % MoS<sub>2</sub>/EP, (<b>c</b>) 1 wt % h-BN/MoS<sub>2</sub>/EP, (<b>d</b>) 2 wt % h-BN/MoS<sub>2</sub>/EP, (<b>e</b>) 5 wt % h-BN/MoS<sub>2</sub>/EP, and (<b>f</b>) 10 wt % h-BN/MoS<sub>2</sub>/EP.</p>
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<p>SEM morphology of worn surfaces of the composites with different contents of h-BN/MoS<sub>2</sub> (<b>a</b>) 1 wt %, (<b>b</b>) 2 wt %, (<b>c</b>) 5 wt %, (<b>d</b>) 10 wt %), (<b>e</b>) the pure EP coating, and (<b>f</b>) the single MoS<sub>2</sub> coating.</p>
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<p>XPS spectra of 5 wt % h-BN/MoS<sub>2</sub> composite coating after friction: (<b>a</b>) C 1s, (<b>b</b>) Mo 3d, (<b>c</b>) S 2p, (<b>d</b>) Si 2p, and (<b>e</b>) Fe 2p.</p>
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<p>Schematic of wear mechanism of EP composite coatings enhanced via h-BN/MoS<sub>2</sub> hybrids.</p>
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18 pages, 11112 KiB  
Article
Dynamic Compressive Behavior, Constitutive Modeling, and Complete Failure Criterion of 30 Vol.% B4C/2024Al Composite
by Qiang Yan, Zhihong Zhao, Tian Luo, Feng Li, Jianjun Zhao, Zhenlong Chao, Sanfeng Liu, Yong Mei and Fengjun Zhou
Materials 2025, 18(5), 1170; https://doi.org/10.3390/ma18051170 - 6 Mar 2025
Viewed by 156
Abstract
This study investigated the compressive behavior of 30 vol.% boron carbide (B4C)/2024 aluminum (Al) composites under quasi-static and dynamic loading at different temperatures. Building on the experimental findings, the Johnson–Cook (JC) model was modified, and a complete failure criterion was proposed. [...] Read more.
This study investigated the compressive behavior of 30 vol.% boron carbide (B4C)/2024 aluminum (Al) composites under quasi-static and dynamic loading at different temperatures. Building on the experimental findings, the Johnson–Cook (JC) model was modified, and a complete failure criterion was proposed. These were validated in Abaqus employing the user subroutine for hardening (VUHARD), which incorporated both the modified JC (MJC) model and the complete failure criterion. Experimental results revealed that strain softening was an important feature of the stress–strain curve. The analysis of mechanisms contributing to yield strength revealed that Taylor and load transfer mechanisms dominated, accounting for 89.6% of the total enhancement. Microstructural analysis identified particle fracture and matrix damage were the primary mechanisms driving material failure. Microcracks mainly propagated through the matrix and interface or directly through the ceramic particles and the matrix. The MJC model demonstrated high accuracy in describing the plastic deformation behavior of the composite, with a mean absolute error (MAE) below 15% under dynamic loading. Further simulation confirmed that finite element analyses using the VUHARD subroutine accurately captured the plastic deformation and crack propagation behaviors of the composite under dynamic loading. This study offers a novel approach to describe the plastic deformation and failure behaviors of ceramic-reinforced aluminum matrix composites under dynamic loading conditions. Full article
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<p>Fabrication, Processing, and Compression Testing of 30 vol.% B<sub>4</sub>C/2024Al Composite. (<b>a</b>) Fabrication through the pressure infiltration process. (<b>b</b>) Schematic of the quasi-static compression test configuration. (<b>c</b>) Schematic of the SHPB test configuration.</p>
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<p>Flowchart of VUHARD subroutine development.</p>
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<p>Processed samples and Compression test results. (<b>a</b>) Low- and high-resolution SEM images of the processed samples. (<b>b</b>) Strain rate versus time curves in SHPB testing at 298.15 K. (<b>c</b>–<b>f</b>) True stress–strain curves at strain rates of 0.01/s, 2000/s, 4000/s, and 6000/s.</p>
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<p>Strengthening mechanisms of the 30 vol.% B<sub>4</sub>C/2024Al composite. (<b>a</b>) Calculated contributions of different strengthening mechanisms to the yield strength enhancement. (<b>b</b>) Comparison of the linear superposition and the sum of squares method for predicting yield strength.</p>
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<p>Damage progression and macro-morphology of the 30 vol.% B<sub>4</sub>C/2024Al composite. (<b>a</b>–<b>c</b>) High-speed images of dynamic compression at 298.15 K and strain rates of 2000/s, 4000/s, and 6000/s. (<b>d</b>) Macro-damage morphology of recovered specimens after compression.</p>
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<p>Damage modes of recovered specimens. (<b>a</b>) 0.01/s, 298.15 K. (<b>b</b>) 6000/s, 298.15 K. (<b>c</b>) 0.01/s, 723.15 K. (<b>d</b>) Two microcrack development modes.</p>
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<p>Construction and parameter calibration of the MJC constitutive equation. (<b>a</b>,<b>b</b>) Evaluation of the coupled effects of temperature and strain rate on flow stress, and determination of the temperature sensitivity coefficient <b><span class="html-italic">s</span></b><span class="html-italic">,</span> and the strain rate sensitivity coefficient <span class="html-italic">m</span>. (<b>c</b>) Calibration of the yield strength parameter <span class="html-italic">A</span> under 0.01/s and 298.15 K. (<b>d</b>) Calibration of parameters <span class="html-italic">B</span>, <span class="html-italic">C</span>, <span class="html-italic">p</span>, and <span class="html-italic">q</span>. (<b>e</b>) Calibration of parameter <span class="html-italic">n</span>. (<b>f</b>) Calibration of parameters <span class="html-italic">C</span><sub>1</sub>, <span class="html-italic">C</span><sub>2</sub>, and <span class="html-italic">C</span><sub>3</sub>.</p>
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<p>Calibration of parameters for the complete failure equation. (<b>a</b>) Strain energy density under experimental conditions. (<b>b</b>) Calibration of parameters <span class="html-italic">D</span><sub>5</sub> and <span class="html-italic">D</span><sub>6</sub>. (<b>c</b>) Calibration of parameters <span class="html-italic">D</span><sub>1</sub>, <span class="html-italic">D</span><sub>2</sub>, <span class="html-italic">D</span><sub>3</sub>, and <span class="html-italic">D</span><sub>4</sub>.</p>
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<p>Fitting results of the MJC constitutive equation. (<b>a</b>–<b>d</b>) Comparison of the stress–strain relationships predicted by the MJC with experimental data at strain rates of 0.01/s, 2000/s, 4000/s, and 6000/s. (<b>e</b>) Mean absolute error of the MJC predictions under dynamic loading conditions.</p>
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<p>Stress–time loading curves at different strain rates.</p>
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<p>Validation of VUHARD subroutine in SHTB finite element analysis. (<b>a</b>–<b>c</b>) Damage morphologies from finite element analysis and experiments at strain rates of 2000/s, 4000/s, and 6000/s. (<b>d</b>–<b>f</b>) Comparison of the stress–strain curves from finite element analysis and experiments at strain rates of 2000/s, 4000/s, and 6000/s.</p>
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17 pages, 7144 KiB  
Article
Synergistic Effects of Hollow Glass Microspheres and Sisal Fibers in Natural Gypsum-Based Composites: Achieving Lightweight, High-Strength, and Aesthetically Superior Construction Materials
by Chang Chen, Yuan Gao, Shaowu Jiu, Yanxin Chen and Yan Liu
Buildings 2025, 15(5), 830; https://doi.org/10.3390/buildings15050830 - 5 Mar 2025
Viewed by 186
Abstract
This study explores the synergistic development of natural gypsum-based composites (NGBCs) with enhanced multifunctional characteristics, employing hollow glass microspheres (HGMs) as density-reducing agents and sisal fibers (SFs) as mechanical reinforcement phases while maintaining superior whiteness properties. Five HGM variants with precisely graded particle [...] Read more.
This study explores the synergistic development of natural gypsum-based composites (NGBCs) with enhanced multifunctional characteristics, employing hollow glass microspheres (HGMs) as density-reducing agents and sisal fibers (SFs) as mechanical reinforcement phases while maintaining superior whiteness properties. Five HGM variants with precisely graded particle sizes (20, 40, 60, 80, and 100 μm) were systematically incorporated into the composite matrix. Sisal fibers with controlled length parameters (10–15 mm) were uniformly dispersed within the gypsum matrix. The multifunctional effects of these additives were comprehensively assessed via integrated mechanical characterization, spectrophotometric whiteness evaluation, and microstructural interrogation. The findings revealed that the incorporation of HGMs resulted in a significant decrease in the NGBC density while concurrently enhancing whiteness; they also exerted an adverse impact on both processability and mechanical properties. Moreover, the fusion of HGMs and SFs within the NGBCs achieved an optimal balance between lightness and strength. The peak density of NGBCs was ascertained to be 1.41 g/cm3, complemented by flexural and compressive strengths of 6.12 and 9.78 MPa, respectively. Such optimizations were realized with HGMs at a particle size of 80 um and a composition of 20 vol.%, alongside sisal fibers present at a concentration of 0.3 vol.%. The current research affords significant revelations regarding the fabrication of architectural gypsum materials that are lightweight, possess high tensile strength, exhibit an aesthetically appealing finish, and demonstrate superior whiteness, presenting a prospective resolution for applications within the high-performance construction sector. Full article
(This article belongs to the Special Issue Innovative Composite Materials in Construction)
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<p>Microscopic morphology of HGMs and SFs. (<b>a</b>) HGMs; (<b>b</b>) surface of HGMs; (<b>c</b>) SFs; and (<b>d</b>,<b>e</b>) surface of SFs.</p>
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<p>Schematic diagram of the experimental flow.</p>
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<p>Densities of NGBCs with different HGM content and particle size.</p>
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<p>The 2 h mechanical properties of NGBCs with different HGM content and particle size.</p>
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<p>The 28 d mechanical properties of NGBCs with different HGM content and particle size.</p>
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<p>Whiteness of NGBCs with different HGM (80 um of particle size) content.</p>
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<p>XRD images of NGBCs with HGM (80 um of particle size and content of 30 vol.%).</p>
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<p>Microscopic images of NGBCs with HGM (80 um of particle size and content of 30 vol.%). (<b>a</b>) NGBCs of single-doped HGMs; (<b>b</b>,<b>c</b>) interface between natural gypsum and HGMs.</p>
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<p>Densities of NGBCs with different HGM and SF content.</p>
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<p>The 2 h mechanical properties of NGBCs with different HGM and SF content.</p>
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<p>The 28 d mechanical properties of NGBCs with different HGM and SF content.</p>
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<p>Whiteness of NGBCs with different SF content.</p>
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<p>XRD images of NGBCs with HGMs (80 um, 20 vol.%) and SFs (0.3 vol.%).</p>
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<p>Microscopic images of NGBCs with HGMs (80 um, 20 vol.%) and SFs (0.3 vol.%).</p>
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28 pages, 7816 KiB  
Article
Machine Learning-Based Measurement and Prediction of Ground Settlement Induced by Shield Tunneling Undercrossing Existing Tunnels in Composite Strata
by Mei Dong, Mingzhe Guan, Kuihua Wang, Yeyao Wu and Yuhan Fu
Sensors 2025, 25(5), 1600; https://doi.org/10.3390/s25051600 - 5 Mar 2025
Viewed by 102
Abstract
To address the issue of insufficient accuracy in traditional settlement prediction methods for shield tunneling undercrossing in composite strata in Hangzhou, this paper proposes a particle swarm optimization (PSO)-based Bidirectional Long Short-Term Memory neural network (Bi-LSTM) prediction model for high-precision dynamic prediction of [...] Read more.
To address the issue of insufficient accuracy in traditional settlement prediction methods for shield tunneling undercrossing in composite strata in Hangzhou, this paper proposes a particle swarm optimization (PSO)-based Bidirectional Long Short-Term Memory neural network (Bi-LSTM) prediction model for high-precision dynamic prediction of ground settlement under small-sample conditions. Shield tunneling is a key method for urban tunnel construction. This paper presents the measurement and prediction of ground settlement caused by shield tunneling undercrossing existing tunnels in composite strata in Hangzhou. The longitudinal ground settlement curve resulting from shield tunnel excavation was analyzed using measured data, and the measured lateral ground settlement was compared with the Peck empirical formula. Using PSO, the performance of three machine learning models in predicting the maximum ground settlement at monitoring points was compared: Long Short-Term Memory neural network (LSTM), Gated Recurrent Unit neural network (GRU), and Bi-LSTM. The linear relationships between different input parameters and between input parameters and the output parameter were analyzed using the Pearson correlation coefficient. Based on this analysis, the model was optimized, and its prediction performance before and after optimization was compared. The results show that the Bi-LSTM model optimized with the PSO algorithm demonstrates superior performance, achieving both accuracy and stability. Full article
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<p>Position relationship between the left line of the new shield tunnel and the existing tunnel: (<b>a</b>) plan view of the position relationship between the new and existing tunnels; (<b>b</b>) vertical position relationship between the left line of the new shield tunnel and the existing tunnel.</p>
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<p>Layout of monitoring points: (<b>a</b>) layout of ground settlement monitoring points for rings 0–25 of the new tunnel; (<b>b</b>) layout of ground settlement monitoring points for rings 25–83 and 600–662 of the new tunnel; (<b>c</b>) layout of ground settlement monitoring points for rings 83–600 of the new tunnel; (<b>d</b>) layout of monitoring points in existing tunnels.</p>
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<p>Longitudinal ground settlement curve before the left line of shield tunnel crosses under the existing tunnel: (<b>a</b>) section of the 25th ring; (<b>b</b>) section of the 58th ring; (<b>c</b>) section of the 75th ring.</p>
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<p>Longitudinal ground settlement curve after the left line of shield tunnel crosses under the existing tunnel: (<b>a</b>) section of the 225th ring; (<b>b</b>) section of the 250th ring.</p>
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<p>Normalized ground settlement: (<b>a</b>) normalized ground settlement values of each ring and the Peck empirical formula curve with i values of 6.5 and 8; (<b>b</b>) average normalized ground settlement and the Peck empirical formula curve with i values of 6.5 and 8.</p>
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<p>Settlement of existing tunnel: (<b>a</b>) longitudinal settlement curve of the existing tunnel in parallel section; (<b>b</b>) longitudinal settlement profile of the existing tunnel in the approach section; (<b>c</b>) longitudinal settlement curve of the existing tunnel in the undercrossing section.</p>
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<p>Deep learning networks: (<b>a</b>) LSTM model structure and its unit structure; (<b>b</b>) GRU unit structure; (<b>c</b>) Bi-LSTM model structure.</p>
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<p>Geological profile of the left line of the shield tunnel.</p>
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<p>Predicted ground settlement for the test set using the LSTM model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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<p>Predicted ground settlement for the test set using the GRU model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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<p>Predicted ground settlement for the test set using the Bi-LSTM model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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<p>Pearson correlation coefficient between parameters.</p>
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<p>Predicted ground settlement for the test set using the optimized LSTM model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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<p>Predicted ground settlement for the test set using the optimized GRU model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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<p>Predicted ground settlement for the test set using the optimized Bi-LSTM model: (<b>a</b>) training results of test set; (<b>b</b>) evaluation results of test set.</p>
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23 pages, 6226 KiB  
Article
Optimizing FSP Parameters for AA5083/SiC Composites: A Comparative Analysis of Taguchi and Regression
by Oritonda Muribwathoho, Velaphi Msomi and Sipokazi Mabuwa
Metals 2025, 15(3), 280; https://doi.org/10.3390/met15030280 - 5 Mar 2025
Viewed by 138
Abstract
The fabrication of AA5083/SiC composites by the friction stir processing (FSP) method is the main objective of this study. The study looks at how the mechanical properties of the composites are affected by three important process parameters: traversal speed, rotational speed, and tilt [...] Read more.
The fabrication of AA5083/SiC composites by the friction stir processing (FSP) method is the main objective of this study. The study looks at how the mechanical properties of the composites are affected by three important process parameters: traversal speed, rotational speed, and tilt angle. The Taguchi L9 design matrix was used to effectively investigate parameter effects, decreasing experimental trials and cutting expenses. Tensile testing measured tensile strength, whereas microhardness tests evaluated hardness. The findings showed that a maximum tensile strength of 243 MPa and a maximum microhardness of 94.80 HV were attained. The findings also showed that the optimal ultimate tensile strength (UTS) and percentage elongation (PE) were achieved at a tilt angle of 2°, a traverse speed of 30 mm per minute, and a rotating speed of 900 rev/min. On the other hand, a slightly greater traverse speed of 45 mm per minute was required to reach maximal microhardness (MH) with the same rotational speed and tilt angle. Analysis of variance (ANOVA) showed that rotational speed has a substantial impact on all mechanical properties, highlighting how important it is for particle dispersion and grain refining. This work is unique in that it systematically optimizes FSP parameters by using regression analysis and the Taguchi technique in addition to ANOVA. This allows for a better understanding of how these factors affect the mechanical properties of SiC-reinforced composites. The findings contribute to advancing the cost-effective fabrication of high-performance metal matrix composites for industrial applications requiring enhanced strength and durability. Full article
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<p>(<b>a</b>) FSW procedure; (<b>b</b>) Drilling of holes and filling them with SiC particles; (<b>c</b>) Using a pinless tool to close the hole; (<b>d</b>) FSP single-pass procedure; (<b>e</b>) Tool with pin tool; (<b>f</b>) Pinless.</p>
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<p>Dimensions and arrangement of the hardness and tensile specimens.</p>
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<p>Results from experiments and regressions for (<b>a</b>) Microhardness (MH), (<b>b</b>) Percentage elongation (PE), and (<b>c</b>) Ultimate tensile strength (UTS).</p>
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<p>Results from experiments and regressions for (<b>a</b>) Microhardness (MH), (<b>b</b>) Percentage elongation (PE), and (<b>c</b>) Ultimate tensile strength (UTS).</p>
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<p>AA5083/SiC composite optical microstructures photographed at 20 × 100 µm magnification with a 100 µm scale bar. (<b>a<sub>1</sub></b>–<b>a<sub>3</sub></b>) Microstructures at 600 rev/min with traverse rates of 30 mm per min, 45 mm per min, and 60 mm per min, respectively, and tilt angles of 1°, 1.75°, and 2°. (<b>b<sub>1</sub></b>–<b>b<sub>3</sub></b>) Microstructures at 900 rev/min with traverse rates of 30 mm per min, 45 mm per min, and 60 mm per min, respectively, and tilt angles of 1.75°, 2°, and 1°. (<b>c<sub>1</sub></b>–<b>c<sub>3</sub></b>) Microstructures having traverse rates of 30 mm per min, 45 mm per min, and 60 mm per min at 1200 rev/min with tilt angles of 2°, 1°, and 1.75°, respectively.</p>
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<p>AA5083/SiC composite S/N ratio and mean plot: (<b>a</b>) Microhardness; (<b>b</b>) Percentage elongation; (<b>c</b>) Ultimate tensile strength.</p>
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<p>Percentage contribution for process parameters.</p>
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<p>Probability Plots; (<b>a</b>) Microhardness, (<b>b</b>) Percentage elongation, (<b>c</b>) Ultimate tensile strength.</p>
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<p>Probability Plots; (<b>a</b>) Microhardness, (<b>b</b>) Percentage elongation, (<b>c</b>) Ultimate tensile strength.</p>
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