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22 pages, 6630 KiB  
Article
Tribological Properties of Nitrate Graphite Foils
by Nikolai S. Morozov, David V. Demchenko, Pavel O. Bukovsky, Anastasiya A. Yakovenko, Vladimir A. Shulyak, Alexandra V. Gracheva, Sergei N. Chebotarev, Irina G. Goryacheva and Viktor V. Avdeev
Nanomaterials 2024, 14(18), 1499; https://doi.org/10.3390/nano14181499 (registering DOI) - 15 Sep 2024
Abstract
This study investigates the tribological properties of graphite foils (GF) with densities of 1.0, 1.3, and 1.6 g/cm3, produced from purified natural graphite of different particle sizes (40–80 μm, 160–200 μm, >500 μm). Surface roughness was measured after cold rolling and [...] Read more.
This study investigates the tribological properties of graphite foils (GF) with densities of 1.0, 1.3, and 1.6 g/cm3, produced from purified natural graphite of different particle sizes (40–80 μm, 160–200 μm, >500 μm). Surface roughness was measured after cold rolling and friction testing at static (0.001 mm/s) and dynamic conditions (0.1 Hz and 1 Hz). Results showed that static friction tests yielded similar roughness values (Sa ≈ 0.5–0.7 μm, Sq ≈ 0.5–1.0 μm) across all densities and particle sizes. Dynamic friction tests revealed increased roughness (Sa from 0.7 to 3.5 μm, Sq from 1.0 to 6.0–7.0 μm). Friction coefficients (µ) decreased with higher sliding speeds, ranging from 0.22 to 0.13. GF with 40–80 μm particles had the lowest friction coefficient (µ = 0.13–0.15), while 160–200 μm particles had the highest (µ = 0.15–0.22). Density changes had minimal impact on friction for the 40–80 μm fraction but reduced friction for the 160–200 μm fraction. Young’s modulus increased with density and decreased with particle size, showing values from 127–274 MPa for 40–80 μm, 104–212 MPa for 160–200 μm, and 82–184 MPa for >500 μm. The stress–strain state in the graphite foil samples was simulated under normal and tangential loads. This makes it possible to investigate the effect of the anisotropy of the material on the stress concentration inside the sample, as well as to estimate the elasticity modulus under normal compression. Structural analyses indicated greater plastic deformation in GF with 40–80 μm particles, reducing coherent-scattering region size from 28 nm to 24 nm. GF samples from 160–200 μm and >500 μm fractions showed similar changes, expanding with density increase from 18 nm to 22 nm. Misorientation angles of GF nanocrystallites decreased from 30° to 27° along the rolling direction (RD). The coherent scattering regions of GF with 40–80 μm particles increased, but no significant changes in the coherent scattering regions were observed for the 160–200 μm and >500 μm fractions during dynamic friction tests. Microstrains and residual macrostresses in GF increased with density for all fractions, expanding under higher friction-induced loads. Higher values of both stresses indicate a higher level of accumulated deformation, which appears to be an additional factor affecting the samples during friction testing. This is reflected in the correlation of the results with the roughness and friction coefficient data of the tested samples. Full article
(This article belongs to the Section 2D and Carbon Nanomaterials)
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Figure 1

Figure 1
<p>Schematic diagram of the experiment: 1—steel counterbody (also green), 2—GF sample (also red), 3—a holder (also blue), orange—fasteners, <span class="html-italic">F</span>—normal load, <span class="html-italic">ω</span>—the frequency ofreciprocating motion.</p>
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<p>Geometry and computational grid for normal load.</p>
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<p>Geometry and computational grid for the tangential loading.</p>
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<p>Topography of the original GF surfaces for the density of 1.0 g/cm<sup>3</sup> (<b>a</b>,<b>d</b>,<b>g</b>), 1.3 g/cm<sup>3</sup> (<b>b</b>,<b>e</b>,<b>h</b>), 1.6 g/cm<sup>3</sup> (<b>c</b>,<b>f</b>,<b>i</b>) by the fractions of 40–80 μm (<b>a</b>–<b>c</b>), 160–200 μsam (<b>d</b>–<b>f</b>), and &gt;500 μm (<b>g</b>–<b>i</b>).</p>
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<p>Topography of the GF surfaces for the density of 1.0 g/cm<sup>3</sup> (<b>a</b>–<b>c</b>), 1.3 g/cm<sup>3</sup> (<b>d</b>–<b>f</b>), and 1.6 g/cm<sup>3</sup> (<b>g</b>–<b>i</b>) obtained from the fractions of 40–80 μm following the experimental studies at the sliding velocity of 1 μm/s (<b>a</b>,<b>d</b>,<b>g</b>), frequency 0.1 Hz (<b>b</b>,<b>d</b>,<b>h</b>), and 1 Hz (<b>c</b>,<b>f</b>,<b>i</b>).</p>
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<p>Relationship between the value of average roughness and the density in the graphite foils by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>) before (the black lines) and after (the colored lines) the frictions testings.</p>
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<p>A typical view of recording static (<b>a</b>) and dynamic (<b>b</b>) friction coefficients on a UMT-3MT laboratory tribometer.</p>
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<p>Relationship between the static (the blue curves) and dynamic (the green and red curves) friction coefficient and the density in the graphite foils by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>).</p>
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<p>(<b>a</b>) Typical case of the relationship between load (1) and unload (2) and the penetration depth for GF material; (<b>b</b>) the elastic modulus of GF in relation to their density and fractional composition; (<b>c</b>) relationship between the compression depth and the applied load for GF, with the density being 1.0 g/cm<sup>3</sup> by the fraction 40–80 μm (the black curve), 160–200 μm (the red curve), &gt;500 μm (the green curve).</p>
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<p>Images of the graphite foil from the 40–80 μm fraction in the original state (<b>a</b>), after the testings of static (<b>b</b>) and dynamic frictions at 0.1 Hz (<b>c</b>) and 1.0 Hz (<b>d</b>).</p>
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<p>Dependences of the vertical displacement of the sample (μm) on the load <span class="html-italic">P</span> (N), obtained numerically (the continuous lines) and experimentally (the dashed lines); (<b>a</b>): linear elasticity, <span class="html-italic">E</span> = 10 MPa (the red line—<math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math>, and the blue line—<math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>), (<b>b</b>): hyper-elasticity, <math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math> (the red line—<span class="html-italic">E</span> = 9.5 MPa, and the blue line—<span class="html-italic">E</span> = 9.0 MPa, the green line—<span class="html-italic">E</span> = 8.5 MPa), (<b>c</b>): hyper-elasticity, <math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math> (the red line—<span class="html-italic">E</span> = 7.5 MPa, the blue line—<span class="html-italic">E</span> = 7 MPa, the green line—<span class="html-italic">E</span> = 6.5 MPa).</p>
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<p>The outcome of the numerical modeling for vertical displacement at 350 μm (von Mises stress distribution over the sample volume, Pa); (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math>, (<b>b</b>) <math display="inline"><semantics> <mrow> <mi>ν</mi> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math>, and distribution of the stress tensor component <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>y</mi> <mi>z</mi> </mrow> </msub> </mrow> </semantics></math>, Pa, in the bar following application of the tangential forces in the middle plane <span class="html-italic">Oyz</span>; (<b>c</b>) isotropic material, (<b>d</b>) anisotropic material.</p>
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<p>The size of the coherent–scattering region in relation to density in the graphite foils, by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>), before (the black lines) and after (the colored lines) the friction testings.</p>
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<p>The misorientation angle size for the nanocrystallites in relation to the density in the graphite foils by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>) in RD, and from similar fractions in TD (<b>d</b>–<b>f</b>) before (the black lines) and after (the colored lines) the friction testings.</p>
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<p>The microstrain values in the nanocrystallites in relation to the density in the graphite foils by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>) before (the black lines) and after (the colored lines) the friction testings.</p>
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<p>The macrostrains values in relation to the density in the graphite foils by the fractions of 40–80 μm (<b>a</b>), 160–200 μm (<b>b</b>), &gt;500 μm (<b>c</b>) in RD, and from similar fractions in TD (<b>d</b>–<b>f</b>) before (the black lines) and after (the colored lines) the friction tests.</p>
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18 pages, 2443 KiB  
Article
Biological Properties of the Mucus and Eggs of Helix aspersa Müller as a Potential Cosmetic and Pharmaceutical Raw Material: A Preliminary Study
by Anna Herman, Patrycja Wińska, Małgorzata Białek and Andrzej P. Herman
Int. J. Mol. Sci. 2024, 25(18), 9958; https://doi.org/10.3390/ijms25189958 (registering DOI) - 15 Sep 2024
Abstract
In recent years, snail mucus (SM) has become popular as an active ingredient in cosmetic and pharmaceutical products. In turn, snail eggs (SEs) also seem to be a promising active compound, but the biological activities of SEs are significantly less known. Therefore, our [...] Read more.
In recent years, snail mucus (SM) has become popular as an active ingredient in cosmetic and pharmaceutical products. In turn, snail eggs (SEs) also seem to be a promising active compound, but the biological activities of SEs are significantly less known. Therefore, our preliminary study aimed to compare the biological activities of the SEs and SM of Helix aspersa Müller. The metabolomic analysis (LC–MS technique), determination of the antimicrobial activity (agar diffusion test, broth microdilution methods), antioxidant activity (ABTS assay), cytotoxicity assay (MTT), and proapoptotic properties (flow cytometry) of the SEs and SM were evaluated. It was found that the SEs and SM contain 8005 and 7837 compounds, respectively. The SEs showed antibacterial activity against S. aureus (MIC 12.5 mg/mL) and P. aeruginosa (MIC 3.12 mg/mL). The EC50 estimation of the antioxidant activity is 89.64 mg/mL and above 100 mg/mL for the SEs and SM, respectively. The SEs also inhibited the cell proliferation of cancer cell lines (HCT-116, MCF-7, HT-29) more strongly compared to the SM. The highest proportion of apoptotic cells in HCT-116 was observed. The reach composition of the compounds in the SEs and SM may be crucial for the creation of new cosmetic and pharmaceutical raw materials with different biological activities. However, further extended studies on the biological activities of H. aspersa-delivered materials are still necessary. Full article
(This article belongs to the Special Issue New Insights in Natural Bioactive Compounds 3.0)
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Figure 1
<p>Radical scavenging activity of SM and SEs in ABTS methods.</p>
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<p>Viability of MCF-7, HT-29, HCT-116, and Vero cell lines after the treatment with SE (<b>A</b>) or SM (<b>B</b>). After 72 h of incubation, MTT test was performed. The data for the treated cells were analyzed by Dunnett’s multiple comparison test as follows: * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, and *** <span class="html-italic">p</span> &lt; 0.001 relative to control served as 100%; ns—not significant.</p>
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<p>Induction of apoptosis in HCT-116 cells. The data were determined by Accuri C6 Plus flow cytometer (BD Biosciences, San Jose, CA, USA) after 72 h of treatment with SE. Cells were stained with annexin V-FITC and PI (propidium iodide). (<b>A</b>) Mean and standard deviation (SD) of necrosis, as well as viable, early, and late apoptosis, as a percentage from three independent experiments each. (<b>B</b>) Representative cytograms for control HTC-116 cells (CTRL) and after treatment with SE. The data for early and late apoptotic cells were analyzed by Dunnett’s multiple comparison test as follows: *** <span class="html-italic">p</span> &lt; 0.001 relative to control; ns—not significant.</p>
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<p>Induction of apoptosis in MCF-7 cells. The data were determined by Accuri C6 Plus flow cytometer after 72 h of treatment with SE. Cells were stained with annexin V-FITC and PI (propidium iodide). (<b>A</b>) Mean and standard deviation (SD) of necrosis, as well as viable, early, and late apoptosis, as a percentage from three independent experiments each. (<b>B</b>) Representative cytograms for control MCF-7 cells (CTRL) and after treatment with SE. The data for early and late apoptotic cells were analyzed by Dunnett’s multiple comparison test as follows: * <span class="html-italic">p</span> &lt; 0.05, and *** <span class="html-italic">p</span> &lt; 0.001 relative to control.</p>
Full article ">
15 pages, 7399 KiB  
Article
Analysis of the Wear Parameters and Microstructure of High-Carbon Steel in Order to Identify Its Tribological Properties
by Janusz Krawczyk, Łukasz Frocisz, Piotr Matusiewicz, Mateusz Kopyściański and Sebastian Lech
Appl. Sci. 2024, 14(18), 8318; https://doi.org/10.3390/app14188318 (registering DOI) - 15 Sep 2024
Abstract
Alloyed high-carbon steels are materials primarily intended for components operating under conditions of intense tribological wear. The carbides present in the microstructure of these materials significantly contribute to improving the wear resistance of such alloys. However, changes in the morphology of these precipitates [...] Read more.
Alloyed high-carbon steels are materials primarily intended for components operating under conditions of intense tribological wear. The carbides present in the microstructure of these materials significantly contribute to improving the wear resistance of such alloys. However, changes in the morphology of these precipitates can considerably alter the wear rate, leading to a deterioration in the properties of the materials. Therefore, this study aims to analyze the influence of several factors on the tribological wear of alloyed high-carbon steel. The research included friction tests under various load conditions and different sliding paths. Additionally, the samples were subjected to heat treatment to change the morphology of the observed precipitates. The tribological tests were conducted in a block-on-ring configuration under dry friction conditions. The tribological tests were analyzed statistically using analysis of variance (ANOVA). The results of the statistical analysis indicated that the primary factor influencing the observed differences between the samples was the heat treatment time of the material. Additionally, there were no significant statistical differences when pressure and friction path were varied. These findings, in conjunction with the SEM studies, allowed for the evaluation of the wear mechanism. The results demonstrated that, within the adopted tribological system, no alterations in the wear mechanism were observed with changes in test parameters. The observed differences in wear properties between the samples were found to be related to their heat treatment. The heat treatment resulted in alterations to the particle size distribution, with the annealing of the material at an elevated temperature leading to the dissolution of finer particles within the material. An increase in the average diameter of the carbide present in the material was observed to improve the wear resistance of the alloy tested. Full article
(This article belongs to the Section Materials Science and Engineering)
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Figure 1
<p>The dilatometric curve for the investigated material.</p>
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<p>Examples of friction coefficient change curves during the test. Variant 100 N-2000 s; (<b>a</b>) 4 h, (<b>b</b>) 8 h, and (<b>c</b>) 12 h.</p>
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<p>Results of the tribological test, (<b>a</b>) mass loss of the samples in correlation to the time of material annealing, (<b>b</b>) average friction coefficient in relation to annealing time, (<b>c</b>) wear depth in relation to the annealing time, and (<b>d</b>) wear depth in relation to force used during the test.</p>
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<p>Surface of samples after tribological testing, area of abrasion, (<b>a</b>)—4 h-100 N-2000 s; (<b>b</b>)—4 h-100 N-4000 s; (<b>c</b>) 4 h-150 N-2000 s; (<b>d</b>) 8 h-100 N-2000 s; (<b>e</b>)—8 h-100 N-4000 s; (<b>f</b>)—8 h-150 N-2000 s; (<b>g</b>)—12 h-100 N-2000 s; (<b>h</b>)—12 h-100 N-4000 s; (<b>i</b>)—12 h-150 N-2000 s.</p>
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<p>Microstructure of the investigated material: (<b>a</b>,<b>d</b>)—4 h annealing; (<b>b</b>,<b>e</b>)—8 h annealing; (<b>c</b>,<b>f</b>)—12 h annealing.</p>
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<p>Frequency distribution of carbide sizes for the test samples. (<b>a</b>) 4 h of annealing, (<b>b</b>) 8 h of annealing, (<b>c</b>) 12 h of annealing.</p>
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<p>Dependence of the average hardness of the tested samples on the annealing time.</p>
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11 pages, 3831 KiB  
Article
A Custom-Developed Device for Testing Tensile Strength and Elasticity of Vascular and Intestinal Tissue Samples for Anastomosis Regeneration Research
by Zoltan Attila Godo, Laszlo Adam Fazekas, Gergo Fritsch, Balazs Szabo and Norbert Nemeth
Sensors 2024, 24(18), 5984; https://doi.org/10.3390/s24185984 (registering DOI) - 15 Sep 2024
Viewed by 159
Abstract
Optimizing the regeneration process of surgically created anastomoses (blood vessels, intestines, nerves) is an important topic in surgical research. One of the most interesting parameter groups is related to the biomechanical properties of the anastomoses. Depending on the regeneration process and its influencing [...] Read more.
Optimizing the regeneration process of surgically created anastomoses (blood vessels, intestines, nerves) is an important topic in surgical research. One of the most interesting parameter groups is related to the biomechanical properties of the anastomoses. Depending on the regeneration process and its influencing factors, tensile strength and other biomechanical features may change during the healing process. Related to the optimal specimen size, the range and accuracy of measurements, and applicability, we have developed a custom-tailored microcontroller-based device. In this paper, we describe the hardware and software configuration of the latest version of the device, including experiences and comparative measurements of tensile strength and elasticity of artificial materials and biopreparate tissue samples. The machine we developed was made up of easily obtainable parts and can be easily reproduced on a low budget. The basic device can apply a force of up to 40 newtons, and can grasp a 0.05–1 cm wide, 0.05–1 cm thick tissue. The length of the test piece on the rail should be between 0.3 and 5 cm. Low production cost, ease of use, and detailed data recording make it a useful tool for experimental surgical research. Full article
(This article belongs to the Special Issue Feature Papers in Biosensors Section 2024)
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<p>Representative picture of the structure of the device from different views. A robust frame is required for stable and accurate operation of the instrument.</p>
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<p>Representative picture of the HJJ-001 type grippers while testing a chicken sciatic nerve (biopreparate).</p>
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<p>Representative superimposed tensile strength measurements stress–strain curve of different suture materials: (<b>A</b>): 4/0 absorbable polyglycolide-poly (e-caprolactone) copolymer suture material (Simfra, Kollsut, North Miami Beach, FL, USA) which we usually use for bowel anastomosis; (<b>B</b>): 5/0 non-absorbable silk suture material (Silk, SMI, Vith, Belgium) using for teaching purposes. (n = 5 per group; L<sub>0</sub> = 8 mm; motor speed: 1.95 mm/s).</p>
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<p>Representative tensile strength measurement stress–strain curves of different tissue biopreparates. The different mechanical properties are easily recognizable, even within a single tissue, as separate ruptures of serosa and mucosa layers (motor speed: 1.95 mm/s).</p>
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<p>Analysis of force–elongation (stress–strain) curve. The initial part of the curve (red) was not included in the slope calculation due to its irregularity (femoral artery biopreparate of a rat; L<sub>0</sub> = 8 mm; motor speed: 1.95 mm/s).</p>
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<p>Representative analysis of the exported data. There were some irregularities in the beginning (even some negative values) so after the gram/newton conversion we applied a filter (0.0196–maximum). The entire filtered curves were divided into two parts: the first-third (0–33%) and the remaining two-thirds (34–100%). The slope of these curves was determined using the following formula in Excel = SLOPE(known_y’s, known_x’s) where x = LΔ and y = applied force. The calculation was equal to the slope of the regression line: slope = tgα = <math display="inline"><semantics> <mrow> <mstyle scriptlevel="0" displaystyle="true"> <mfrac> <mrow> <mo>∑</mo> <mfenced separators="|"> <mrow> <mi>x</mi> <mo>−</mo> <mover accent="true"> <mrow> <mi>x</mi> </mrow> <mo>¯</mo> </mover> </mrow> </mfenced> <mo>∗</mo> <mfenced separators="|"> <mrow> <mi>y</mi> <mo>−</mo> <mover accent="true"> <mrow> <mi>y</mi> </mrow> <mo>¯</mo> </mover> </mrow> </mfenced> </mrow> <mrow> <mo>∑</mo> <msup> <mrow> <mfenced separators="|"> <mrow> <mi>x</mi> <mo>−</mo> <mover accent="true"> <mrow> <mi>x</mi> </mrow> <mo>¯</mo> </mover> </mrow> </mfenced> </mrow> <mrow> <mn>2</mn> </mrow> </msup> </mrow> </mfrac> </mstyle> </mrow> </semantics></math>. (5/0 non-absorbable silk suture material (Silk, SMI, Belgium); L<sub>0</sub> = 8 mm; motor speed: 1.95 mm/s.)</p>
Full article ">
12 pages, 3779 KiB  
Article
A Silver Modified Nanosheet Self-Assembled Hollow Microsphere with Enhanced Conductivity and Permeability
by Fangmin Wang, Xue Dong, Yuzhen Zhao, Zemin He, Wenqi Song, Chunsheng Li, Jiayin Li, Jianfeng Huang and Zongcheng Miao
Molecules 2024, 29(18), 4384; https://doi.org/10.3390/molecules29184384 (registering DOI) - 15 Sep 2024
Viewed by 179
Abstract
The utilization of sheet structure composites as a viable conductive filler has been implemented in polymer-based electromagnetic shielding materials. However, the development of an innovative sheet structure to enhance electromagnetic shielding performance remains a significant challenge. Herein, we propose a novel design incorporating [...] Read more.
The utilization of sheet structure composites as a viable conductive filler has been implemented in polymer-based electromagnetic shielding materials. However, the development of an innovative sheet structure to enhance electromagnetic shielding performance remains a significant challenge. Herein, we propose a novel design incorporating silver-modified nanosheet self-assembled hollow spheres to optimize their performance. The unique microporous structure of the hollow composite, combined with the self-assembled surface nanosheets, facilitates multiple reflections of electromagnetic waves, thereby enhancing the dissipation of electromagnetic energy. The contribution of absorbing and reflecting electromagnetic waves in hollow nanostructures could be attributed to both the inner and outer surfaces. When multiple reflection attenuation is implemented, the self-assembled stack structure of nanosheets outside the composite material significantly enhances the occurrence of multiple reflections, thereby effectively improving its shielding performance. The structure also facilitates multiple reflections of incoming electromagnetic waves at the internal and external interfaces of the material, thereby enhancing the shielding efficiency. Simultaneously, the incorporation of silver particles can enhance conductivity and further augment the shielding properties. Finally, the optimized Ag/NiSi-Ni nanocomposites can demonstrate superior initial permeability (2.1 × 10−6 H m−1), saturation magnetization (13.2 emu g−1), and conductivity (1.2 × 10−3 Ω•m). This work could offer insights for structural design of conductive fillers with improved electromagnetic shielding performance. Full article
(This article belongs to the Section Nanochemistry)
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Figure 1
<p>XRD patterns of NiSi-Ni (OH)<sub>2</sub>, NiSi-Ni, and Ag/NiSi-Ni.</p>
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<p>The SEM images of NiSi–Ni(OH)<sub>2</sub> (<b>a</b>,<b>b</b>), NiSi–Ni (<b>c</b>,<b>d</b>), and Ag/NiSi-Ni (<b>e</b>,<b>f</b>).</p>
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<p>The TEM and HRTEM images of NiSi–Ni(OH)<sub>2</sub> (<b>a</b>–<b>c</b>); NiSi–Ni (<b>d</b>–<b>f</b>); and Ag/NiSi-Ni (<b>g</b>–<b>i</b>).</p>
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<p>Nitrogen adsorption, desorption isotherms (<b>a</b>), and pore diameter distributions (<b>b</b>) of NiSi-Ni (OH)<sub>2</sub>, NiSi-Ni, and Ag/NiSi-Ni.</p>
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<p>Hysteresis loops (<b>a</b>) and initial magnetization curves (<b>b</b>) of NiSi-Ni and Ag/NiSi-Ni.</p>
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<p>The SEM images of Ag/NiSi–Ni-1 (<b>a</b>), Ag/NiSi–Ni-2 (<b>b</b>), and Ag/NiSi–Ni-3 (<b>c</b>).</p>
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<p>Volume resistivity of Ag/NiSi–Ni–1, Ag/NiSi–Ni–2, and Ag/NiSi–Ni–3.</p>
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<p>Absorption, reflection, and transmission mechanisms of high-frequency electromagnetic waves in nanosheet self-assembled hollow sphere structure particles.</p>
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<p>Schematic illustration of the preparation process of Ag/NiSi-Ni.</p>
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15 pages, 9533 KiB  
Article
Photo-Crosslinked Pro-Angiogenic Hydrogel Dressing for Wound Healing
by Wang Zhang, Shuyi Qian, Jia Chen, Tianshen Jian, Xuechun Wang, Xianmin Zhu, Yixiao Dong and Guoping Fan
Int. J. Mol. Sci. 2024, 25(18), 9948; https://doi.org/10.3390/ijms25189948 (registering DOI) - 15 Sep 2024
Viewed by 148
Abstract
Severe burns are one of the most devastating injuries, in which sustained inflammation and ischemia often delay the healing process. Pro-angiogenic growth factors such as vascular endothelial growth factor (VEGF) have been widely studied for promoting wound healing. However, the short half-life and [...] Read more.
Severe burns are one of the most devastating injuries, in which sustained inflammation and ischemia often delay the healing process. Pro-angiogenic growth factors such as vascular endothelial growth factor (VEGF) have been widely studied for promoting wound healing. However, the short half-life and instability of VEGF limit its clinical applications. In this study, we develop a photo-crosslinked hydrogel wound dressing from methacrylate hyaluronic acid (MeHA) bonded with a pro-angiogenic prominin-1-binding peptide (PR1P). The materials were extruded in wound bed and in situ formed a wound dressing via exposure to short-time ultraviolet radiation. The study shows that the PR1P-bonded hydrogel significantly improves VEGF recruitment, tubular formation, and cell migration in vitro. Swelling, Scanning Electron Microscope, and mechanical tests indicate the peptide does not affect the overall mechanical and physical properties of the hydrogels. For in vivo studies, the PR1P-bonded hydrogel dressing enhances neovascularization and accelerates wound closure in both deep second-degree burn and full-thickness excisional wound models. The Western blot assay shows such benefits can be related to the activation of the VEGF–Akt signaling pathway. These results suggest this photo-crosslinked hydrogel dressing efficiently promotes VEGF recruitment and angiogenesis in skin regeneration, indicating its potential for clinical applications in wound healing. Full article
(This article belongs to the Special Issue Advanced Research on Wound Healing 2.0)
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<p>Fabrication of an injectable HA-P hydrogel wound dressing. (<b>A</b>) Schematic illustration of the synthesis of MeHA and in situ crosslinking with cysteine-modified PR1P to form a hydrogel wound dressing. (<b>B</b>) Real-time crosslinking rheological measurements of HA and HA-P hydrogels (0.5% <span class="html-italic">w</span>/<span class="html-italic">v</span>) with 30 s exposure to UV radiation. (<b>C</b>) Compressive modulus of HA hydrogels with different material concentrations (gelation with 30 s exposure to UV radiation). (<b>D</b>) Compressive modulus of HA and HA-P hydrogels (0.5% <span class="html-italic">w</span>/<span class="html-italic">v</span>, with 30 s exposure to UV radiation) (mean ± SD, n = 6, <span class="html-italic">** p &lt;</span> 0.01, <span class="html-italic">**** p &lt;</span> 0.0001, ns, not statistically significant).</p>
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<p>Characterization of HA and HA-P hydrogels. (<b>A</b>,<b>B</b>) SEM micrographs and quantification of the average pore size of freeze-dried HA hydrogels (0.5% <span class="html-italic">w</span>/<span class="html-italic">v</span>) with 30 s, 60 s, and 90 s of UV exposure. (<b>C</b>,<b>D</b>) SEM micrographs and quantification of the average pore size of HA and HA-P hydrogels (0.5% <span class="html-italic">w</span>/<span class="html-italic">v</span>, with 30 s of UV exposure). (<b>E</b>,<b>F</b>) Swelling ratios of HA hydrogels with various UV exposure times and material concentrations. (<b>G</b>) Swelling ratios of HA and HA-P hydrogels (0.5% <span class="html-italic">w</span>/<span class="html-italic">v</span>, with 30 s of UV exposure) (mean ± SD, n = 3, *** <span class="html-italic">p</span> &lt; 0.001, <span class="html-italic">**** p</span> &lt; 0.0001, ns, not statistically significant, scale bar, 100 μm).</p>
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<p>VEGF recruitment and in vitro angiogenic effect of HA-P hydrogels. (<b>A</b>) Schematic illustration of VEGF recruitment assay. (<b>B</b>) Quantitative analysis of the maintained VEGF within hydrogels shows the HA-P hydrogel binds more VEGF than HA hydrogel does (n = 8). (<b>C</b>) Representative images of cell migration in a scratch wound healing assay after 0, 6, 12, and 24 h. (<b>D</b>) Quantitative analysis of the migration ratio shows HA-P hydrogel loaded with VEGF significantly promotes cell migration compared with the other groups. (<b>E</b>) Representative images of the tube formation of HUVECs. (<b>F</b>,<b>G</b>) Quantitative analysis of capillary length and the number of branch points of the tubule network. The capillary length and branch points in HA-P hydrogels are significantly higher than in the other groups (mean ± SD, n = 3, <span class="html-italic">** p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, **** <span class="html-italic">p</span> &lt; 0.0001, scale bar, 200 μm).</p>
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<p>HA-P hydrogel dressing promotes wound regeneration in burns. (<b>A</b>) Representative photos exhibit the wound healing process. (<b>B</b>) Quantitative analysis of residual wound area (%) up to 14 days. HA-P hydrogel treatment shows significant acceleration of healing compared to the control group after day 6. (<b>C</b>) Representative images of H&amp;E staining and (<b>D</b>) Masson’s trichrome staining of the wounds at 14 days post-wounding (scale bar, 500 μm). (<b>E</b>) Quantitative analysis of epithelium thickness and (<b>F</b>) collagen density indicates less epidermis hyperplasia and increased collagen deposition in the HA-P hydrogel treatment group (mean ± SD, n = 8–10, <span class="html-italic">* p</span> &lt; 0.05, <span class="html-italic">** p</span> &lt; 0.01, ns, not statistically significant).</p>
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<p>HA-P hydrogel dressing enhances angiogenesis and reduces myofibroblasts in burns. (<b>A</b>) Representative images of the CD31<sup>+</sup> staining (green) of different groups at day 14 post-wounding. The nucleus was stained with DAPI (blue). (<b>B</b>,<b>C</b>) Stereological quantification of the surface area and length density of vasculature demonstrates a significant enhancement in angiogenesis for HA-P hydrogel compared with the control group. (<b>D</b>) Representative images of α-SMA<sup>+</sup> staining (red) at day 14 post-wounding. The nucleus was stained with DAPI (blue). (<b>E</b>) Quantitative analysis of the positive area of α-SMA shows the HA-P hydrogel treatment significantly reduces myofibroblasts’ regeneration (mean ± SD, n = 8–10, <span class="html-italic">** p</span> &lt; 0.01, **** <span class="html-italic">p</span> &lt; 0.0001, ns, not statistically significant, scale bar, 100 μm).</p>
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<p>HA-P hydrogel dressing promoted angiogenesis via activation of the VEGF–Akt signaling pathway. (<b>A</b>) Schematic illustration of the molecular mechanism for HA-P hydrogel dressing which activates the VEGF–Akt signaling pathway in wound healing. (<b>B</b>) Representative images of Western blotting of Akt, p-Akt, and VEGFA in wounds at day 14 post-wounding. (<b>C</b>,<b>D</b>) Quantitative results of Western blotting show that the HA-P hydrogel treatment significantly increases the relative protein expression level of VEGFA and the relative expression ratio of p-Akt/Akt (mean ± SD, n = 8–10, <span class="html-italic">* p</span> &lt; 0.05, ns, not statistically significant).</p>
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<p>HA-P hydrogel dressing promotes wound healing in a full-thickness excisional wound model. (<b>A</b>) Representative images of the healing process up to 14 days post-wounding. (<b>B</b>) Wound closure curves of different groups show a significant acceleration of healing with the HA-P hydrogel treatment compared to the HA hydrogel and control group from day 4. (<b>C</b>) Representative images of CD31<sup>+</sup> (green) and α-SMA<sup>+</sup> (red) staining at day 14 post-wounding. The nucleus was stained with DAPI (blue). (<b>D</b>,<b>E</b>) Quantitative analysis indicates the HA-P hydrogel treatment significantly improves the angiogenesis and (<b>F</b>) reduces myofibroblasts’ regeneration (mean ± SD, n = 6, ** <span class="html-italic">p</span> &lt; 0.01, **** <span class="html-italic">p</span> &lt; 0.0001, ns, not statistically significant, scale bar, 100 μm).</p>
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14 pages, 6981 KiB  
Article
Corrosion Behaviour of Weld Metal of Ultra-High-Strength Steel Weldments in a Sodium Chloride Aqueous Solution
by Mariana Ilieva, Danail Gospodinov, Nikolay Ferdinandov and Rossen Radev
Materials 2024, 17(18), 4534; https://doi.org/10.3390/ma17184534 (registering DOI) - 15 Sep 2024
Viewed by 188
Abstract
As high-strength and ultra-high-strength steels are widely used in all kinds of modern welded constructions, a lot of research is carried out to investigate the mechanical properties of the weldments of these steels, but there is little information on such important characteristics as [...] Read more.
As high-strength and ultra-high-strength steels are widely used in all kinds of modern welded constructions, a lot of research is carried out to investigate the mechanical properties of the weldments of these steels, but there is little information on such important characteristics as their corrosion behaviour. This research focuses on the corrosion behaviour of the weld metal of the weldments of S906QL and S700MC steels. The weld metal was tested electrochemically in a 3.5% NaCl aqueous solution via a potentiodynamic scan to determine the corrosion rate and its dependence on the welding gap. No influence of the welding gap on the corrosion rate was found, but the experimental results suggested that the corrosion rate depended on the chemical composition of the filler material and the microstructure of the weld metal. Full article
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<p>Macrostructure of the weldments, longitudinal section.</p>
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<p>Macrostructure of weldments of S960QL, cross-section.</p>
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<p>Macrostructure of weldments of S700MC, cross-section.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S960QL at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S960QL at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S700MC at two different magnifications.</p>
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<p>Microstructure of the base metal (BM) and weld metal (WM) of the weldments of S700MC at two different magnifications.</p>
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<p>Open circuit potential of S960QL and weld metal of weldments of S960QL in a 3.5% NaCl water solution at room temperature.</p>
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<p>Open circuit potential of S700MC and weld metal of weldments of S700MC in a 3.5% NaCl water solution at room temperature.</p>
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<p>Polarisation curves of S960QL and weld metal of weldments of S960QL in a 3.5% NaCl water solution at room temperature.</p>
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<p>Polarisation curves of S700MC and weld metal of weldments of S700MC in a 3.5% NaCl water solution at room temperature.</p>
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18 pages, 3680 KiB  
Article
Innovative PEEK in Dentistry of Enhanced Adhesion and Sustainability through AI-Driven Surface Treatments
by Mattew A. Olawumi, Francis T. Omigbodun, Bankole I. Oladapo, Temitope Olumide Olugbade and David B. Olawade
Bioengineering 2024, 11(9), 924; https://doi.org/10.3390/bioengineering11090924 (registering DOI) - 14 Sep 2024
Viewed by 351
Abstract
This research investigates using Polyether ether ketone (PEEK) in dental prosthetics, focusing on enhancing the mechanical properties, adhesion capabilities, and environmental sustainability through AI-driven data analysis and advanced surface treatments. The objectives include improving PEEK’s adhesion to dental types of cement, assessing its [...] Read more.
This research investigates using Polyether ether ketone (PEEK) in dental prosthetics, focusing on enhancing the mechanical properties, adhesion capabilities, and environmental sustainability through AI-driven data analysis and advanced surface treatments. The objectives include improving PEEK’s adhesion to dental types of cement, assessing its biocompatibility, and evaluating its environmental impact compared to traditional materials. The methodologies employed involve surface treatments such as plasma treatment and chemical etching, mechanical testing under ASTM standards, biocompatibility assessments, and lifecycle analysis. AI models predict and optimize mechanical properties based on extensive data. Significant findings indicate that surface-treated PEEK exhibits superior adhesion properties, maintaining robust mechanical integrity with no cytotoxic effects and supporting its use in direct contact with human tissues. Lifecycle analysis suggests PEEK offers a reduced environmental footprint due to lower energy-intensive production processes and recyclability. AI-driven analysis further enhances the material’s performance prediction and optimization, ensuring better clinical outcomes. The study concludes that with improved surface treatments and AI optimization, PEEK is a promising alternative to conventional dental materials, combining enhanced performance with environmental sustainability, paving the way for broader acceptance in dental applications. Full article
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<p>Advanced surface modification of PEEK for enhanced dental implants.</p>
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<p>Stress–strain behaviour of PEEK compared to traditional dental materials.</p>
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<p>(<b>a</b>) Fatigue resistance of PEEK under cyclic loading; (<b>b</b>) wear resistance of PEEK under simulated oral conditions; (<b>c</b>) biocompatibility indicators of PEEK over time; and (<b>d</b>) microbial colonisation on PEEK and titanium surfaces.</p>
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<p>Bar graph showing the thermal conductivity of PEEK compared to other dental materials such as titanium, zirconia, and composite resin.</p>
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<p>(<b>a</b>) Line graph depicting the fatigue resistance of PEEK under cyclic loading conditions; (<b>b</b>) line graph showing the wear resistance of PEEK under simulated oral conditions; (<b>c</b>) line graph displaying long-term biocompatibility indicators, tracking inflammation markers and tissue integration over time; (<b>d</b>) bar graph comparing microbial colonization rates on PEEK and titanium surfaces.</p>
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<p>(<b>a</b>) Bar graph showing surface energy comparisons before and after surface treatments on PEEK; (<b>b</b>) graph displaying the impact of surface treatment on the bond strength of PEEK to dental types of cement; (<b>c</b>) line graph illustrating the effect of aging on the mechanical properties of PEEK in dental applications; (<b>d</b>) patient satisfaction scores statistical representations comparing patient satisfaction related to comfort, function, and aesthetics of PEEK versus other materials.</p>
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<p>(<b>a</b>) Surface energy comparison before and after surface treatments on PEEK; (<b>b</b>) impact of surface treatment on the bond strength of PEEK to dental types of cement; (<b>c</b>) effect of aging on the mechanical properties of PEEK in dental applications; and (<b>d</b>) patient satisfaction scores with PEEK-based prosthetics vs. traditional materials.</p>
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<p>(<b>a</b>) Thermal stability charts; (<b>b</b>) water absorption curves; (<b>c</b>) fatigue cycle graphs.</p>
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16 pages, 10120 KiB  
Article
Insight into the Structural and Performance Correlation of Photocatalytic TiO2/Cu Composite Films Prepared by Magnetron Sputtering Method
by Kun Lu, Miao Sun, Yaohong Jiang, Xinmeng Wu, Lijun Zhao and Junhua Xu
Catalysts 2024, 14(9), 621; https://doi.org/10.3390/catal14090621 (registering DOI) - 14 Sep 2024
Viewed by 260
Abstract
Photocatalysis technology, as an efficient and safe environmentally friendly purification technique, has garnered significant attention and interest. Traditional TiO2 photocatalytic materials still face limitations in practical applications, hindering their widespread adoption. The research prepared TiO2/Cu films with different Cu contents [...] Read more.
Photocatalysis technology, as an efficient and safe environmentally friendly purification technique, has garnered significant attention and interest. Traditional TiO2 photocatalytic materials still face limitations in practical applications, hindering their widespread adoption. The research prepared TiO2/Cu films with different Cu contents using a magnetron sputtering multi-target co-deposition technique. The incorporation of Cu significantly enhances the antibacterial properties and visible light response of the films. The effects of different Cu contents on the microstructure, surface morphology, wettability, antibacterial properties, and visible light response of the films were investigated using an X-ray diffractometer, X-ray photoelectron spectrometer, field emission scanning electron microscope, confocal laser scanning microscope, Ultraviolet–visible spectrophotometer, and contact angle goniometer. The results showed that the prepared TiO2/Cu films were mainly composed of the rutile TiO2 phase and face-center cubic Cu phase. The introduction of Cu affected the crystal orientation of TiO2 and refined the grain size of the films. With the increase in Cu content, the surface roughness of the films first decreased and then increased. The water contact angle of the films first increased and then decreased, and the film exhibited optimal hydrophobicity when the Cu target power was 10 W. The TiO2/Cu films showed good antibacterial properties against Escherichia coli and Staphylococcus aureus. The introduction of Cu shifted the absorption edge of the films to the red region, significantly narrowed the band gap width to 2.5 eV, and broadened the light response range of the films to the visible light region. Full article
32 pages, 3251 KiB  
Review
Research Progress on Rolling Forming of Tungsten Alloy
by Jun Cao, Jie Xia, Xiaoyu Shen, Kexing Song, Yanjun Zhou and Chengqiang Cui
Materials 2024, 17(18), 4531; https://doi.org/10.3390/ma17184531 (registering DOI) - 14 Sep 2024
Viewed by 216
Abstract
Tungsten is a metal with many unique characteristics, such as a high melting point, high hardness, high chemical stability, etc. It is widely used in high-end manufacturing, new energy, the defense industry, and other fields. However, tungsten also has room-temperature brittleness, recrystallization brittleness, [...] Read more.
Tungsten is a metal with many unique characteristics, such as a high melting point, high hardness, high chemical stability, etc. It is widely used in high-end manufacturing, new energy, the defense industry, and other fields. However, tungsten also has room-temperature brittleness, recrystallization brittleness, and other shortcomings due to the adjustment of the composition and organizational structure, such as the addition of alloying elements, adjusting the phase ratio, the use of heat treatment and deformation strengthening, etc. Its performance can be improved to meet the requirements for use in different fields. At present, the main production method of tungsten alloy is powder metallurgy. The use of a rolling open billet rotary forging–stretching process can improve production efficiency and product quality, but in actual production, due to the combined effects of various factors, such as elastic deformation of rolling elements, plastic deformation of the rolled material, etc., the mechanical properties of tungsten plates and bars are often difficult to control effectively, seriously affecting rolling stability and production efficiency. For this reason, researchers have conducted extensive and deep research and optimization on the rolling process of tungsten alloys, including establishing mathematical models, performing numerical simulations, optimizing process parameters, etc., providing important references for the rolling and forming of tungsten alloys. Meanwhile, the material properties are greatly influenced by the microstructure, and the evolution of the microstructure can be well quantified by some advanced characterization techniques, such as SEM, TEM, EBSD, etc., so that certain properties of tungsten can be obtained by controlling the texture evolution. In conclusion, this paper comprehensively summarizes the research progress of tungsten alloy roll forming and provides an important reference for further improving the processing performance and production efficiency of tungsten alloy. Full article
17 pages, 4355 KiB  
Article
One-Step-Modified Biochar by Natural Anatase for Eco-Friendly Cr (VI) Removal
by Yinxin Zhao, Ye Wang, Wenqing Xie, Zitong Li, Yunzhu Zhou, Runjie Qin, Lei Wang, Jiqiang Zhou and Guiping Ren
Sustainability 2024, 16(18), 8056; https://doi.org/10.3390/su16188056 (registering DOI) - 14 Sep 2024
Viewed by 283
Abstract
The global serious pollution situation urgently needs green, efficient, and sustainable development methods to achieve heavy metal pollution control. The photocatalytic properties of anatase are sufficient to achieve pollution control by providing photoelectrons to harmful heavy metals. However, since natural anatase particles tend [...] Read more.
The global serious pollution situation urgently needs green, efficient, and sustainable development methods to achieve heavy metal pollution control. The photocatalytic properties of anatase are sufficient to achieve pollution control by providing photoelectrons to harmful heavy metals. However, since natural anatase particles tend to agglomerate and deactivate in water, most studies have been conducted to prepare TiO2–biochar nanocomposites using chemical synthesis methods. In the present study, we utilized pyrolytic sintering to load natural anatase onto biochar to obtain natural anatase–biochar (TBC) composites. Characterization tests, such as X-ray diffraction (XRD), scanning electron microscopy (SEM), and X-ray photoelectron spectroscopy (XPS), showed that anatase was uniformly partitioned into the surface and pores of biochar without destroying the lattice structure. Due to its photocatalytic properties, TBC degraded Cr (VI) by 99.63% under light conditions. This is 1.58 times higher than the dark condition. Zeta potential showed that the surface of the TBC was positively charged under acidic conditions. The charge attraction between TBC and chromium salt was involved in the efficient degradation of Cr (VI). Different sacrificial agents as well as gas purge experiments demonstrated that photoelectrons (e) and superoxide radicals (O2) dominated the degradation of Cr (VI). TBC has the characteristics of high efficiency, stability, and sustainability. This may provide a new idea for the preparation of photocatalytic materials and the realization of environmental protection and sustainable development through heavy metal pollution control. Full article
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<p>SEM images of (<b>a</b>) raw corn cob material and (<b>b</b>,<b>d</b>) corn cob biochar (BC); (<b>c</b>) EDX spectra of BC; (<b>e</b>,<b>f</b>) EDX elemental mapping images of BC; (<b>g</b>,<b>h</b>) SEM images of the anatase–biochar composite (TBC); (<b>i</b>) EDX spectra of TBC; (<b>j</b>,<b>k</b>,<b>l</b>) the EDX elemental mapping images of TBC.</p>
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<p>XRD patterns of TBC (biochar–TiO<sub>2</sub>), BC (biochar), and TiO<sub>2</sub> (anatase).</p>
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<p>(<b>a</b>) XPS full spectra of TBC and BC; fine spectra of TBC on C 1s (<b>b</b>), O 1s (<b>c</b>), and Ti 2p (<b>d</b>).</p>
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<p>(<b>a</b>) Cr (VI) degradation process of TBC, BC, and anatase; (<b>b</b>) primary adsorption kinetic fitting; (<b>c</b>,<b>d</b>) secondary adsorption kinetic fitting.</p>
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<p>(<b>a</b>) Cr (VI) degradation efficiency of TBC at different initial pH; (<b>b</b>) zeta potential of TBC, BC, and anatase.</p>
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<p>(<b>a</b>) Kinetics of Cr (VI) degradation of TBC with different sacrificial agents (in light); (<b>b</b>) Cr (VI) degradation of TBC with different gases (in light).</p>
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<p>Time–current curves (<b>a</b>) and (<b>b</b>) Nyquist plots of TBC, BC, and anatase (in light).</p>
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<p>Cyclic degradation curves of Cr (VI) in TBC cleaned with (<b>a</b>) H<sub>2</sub>O, (<b>b</b>) HCl, (<b>c</b>) NaOH, and (<b>d</b>) stability of TBC.</p>
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<p>Mechanism of reduction in the solution of Cr (VI).</p>
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17 pages, 6795 KiB  
Article
Experimental and Modeling Analysis of Polypropylene Fiber Reinforced Concrete Subjected to Alkali Attack and Freeze–Thaw Cycling Effect
by Yuxiang Huang, Yongcheng Ji, Jingchen Wang, Zihao Wang, Bosong Yu and Siyu Zhang
Materials 2024, 17(18), 4529; https://doi.org/10.3390/ma17184529 (registering DOI) - 14 Sep 2024
Viewed by 322
Abstract
The durability of concrete materials in harsh environmental conditions, particularly in cold regions, has garnered significant attention in civil engineering research in recent years. Concrete structures in these areas are often damaged by the combined effects of alkali–silica reaction (ASR) and freeze–thaw cycles, [...] Read more.
The durability of concrete materials in harsh environmental conditions, particularly in cold regions, has garnered significant attention in civil engineering research in recent years. Concrete structures in these areas are often damaged by the combined effects of alkali–silica reaction (ASR) and freeze–thaw cycles, leading to structural cracks and significant safety hazards. Numerous studies have demonstrated that polypropylene fiber concrete exhibits excellent crack resistance and durability, making it promising for applications in cold regions. This study elucidates the impact of alkali content on concrete durability by comparing the mechanical properties and durability of different alkali–aggregate concretes. The principal experimental methodologies employed include freeze–thaw cycle experiments, which examine patterns of mass loss; fluctuations in the dynamic modulus of elasticity; and changes in mechanical properties before and after freeze cycles. The findings indicate that increased alkali content in concrete reduces its strength and durability. At 100% alkali–aggregate content, compressive strength decreases by 35.5%, flexural strength by 32.9%, mass loss increases by 35.85%, relative dynamic elastic modulus by 39.4%, and residual strength by 97.28%, indicating higher alkali content leads to diminished durability. Additionally, this paper introduces a constitutive damage model, validated by a strong correlation with experimental stress–strain curves, to effectively depict the stress–strain relationship of concrete under varying alkali contents. This research contributes to a broader understanding of concrete durability in cold climates and guides the selection of materials for sustainable construction in such environments. Full article
(This article belongs to the Section Construction and Building Materials)
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<p>Aggregate used in the experiment: (<b>a</b>) crushed stone; (<b>b</b>) recycled concrete; (<b>c</b>) basalt; (<b>d</b>) granite.</p>
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<p>Gel precipitation of (<b>a</b>) C100, (<b>b</b>) R100, (<b>c</b>) B100, and (<b>d</b>) G100 (ordered from <b>left</b> to <b>right</b>) after soaking in 0.1 mol/L NaOH solution.</p>
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<p>Particle size distribution curve of aggregate.</p>
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<p>Parallel bar system.</p>
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<p>Uniaxial stress–strain curve of recycled concrete.</p>
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<p>The relationship between parameters and alkali–aggregate content r: (<b>a</b>) variation of parameter a with alkali aggregate; (<b>b</b>) variation of parameter b with alkali aggregate; (<b>c</b>) variation of E with r alkali aggregate.</p>
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<p>Test curve and theoretical calculation curve: (<b>a</b>) The fitting curve and C100 test curve; (<b>b</b>) The fitting curve and R30 test curve; (<b>c</b>) The fitting curve and R60 test curve; (<b>d</b>) The fitting curve and R100 test curve.</p>
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<p>Concrete compressive and flexural strength of each group.</p>
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<p>The mass loss rate of concrete: (<b>a</b>) mass loss rate of R group; (<b>b</b>) mass loss rate of B group; (<b>c</b>) mass loss rate of G group.</p>
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<p>Relative dynamic elastic modulus loss rate of concrete: (<b>a</b>) relative dynamic elastic modulus loss rate of R group; (<b>b</b>) relative dynamic elastic modulus loss rate of B group; (<b>c</b>) relative dynamic elastic modulus loss rate of G group.</p>
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<p>The strength loss rate of concrete: (<b>a</b>) strength loss rate of the R group; (<b>b</b>) strength loss rate of the B group; (<b>c</b>) strength loss rate of the G group.</p>
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<p>Flexural strength loss rate prediction curve at different freeze–cycle times.</p>
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16 pages, 4892 KiB  
Article
Fabrication of Silicon Carbide Nanoparticles Using Pulsed Laser Ablation in Liquid and Viscosity Optimization via Solvent Tuning
by Saeid Heidarinassab, Anesu Nyabadza, Inam Ul Ahad and Dermot Brabazon
Materials 2024, 17(18), 4527; https://doi.org/10.3390/ma17184527 (registering DOI) - 14 Sep 2024
Viewed by 224
Abstract
In this study, silicon carbide nanoparticles (NPs) were produced via pulsed laser ablation in liquid, aiming to investigate the influence of processing parameters on the properties of the resultant NPs and their applicability for inkjet printing. The results revealed an increase in NP [...] Read more.
In this study, silicon carbide nanoparticles (NPs) were produced via pulsed laser ablation in liquid, aiming to investigate the influence of processing parameters on the properties of the resultant NPs and their applicability for inkjet printing. The results revealed an increase in NP concentration with increasing laser power, but the maximal absorbance in the case of 0.743 and 1.505 W is lower than that for 1.282 W laser. Dynamic light scattering was employed to determine the size distribution of the NPs, demonstrating a range of 89 to 155 nm in diameter. Notably, an inverse relationship was established between increasing laser scanning speed and pulse repetition rate (PRR) and the mean size of the NPs. Higher PRR and laser power exhibited an augmentation in the concentration of NPs. Conversely, an increase in scanning speed resulted in a reduction in NP concentration. Based on FTIR, data formation of SiC NPs based on the target material is the most dominant behavior observed followed by an amount of oxidation of the NPs. Examination of the resulting NPs through field emission scanning electron microscopy equipped with energy-dispersive X-ray analysis (EDX) unveiled a predominantly spherical morphology, accompanied by particle agglomeration in some cases, and the elemental composition showed silicon, carbon, and some oxygen present in the resulting NPs. Furthermore, the modulation of colloidal solution viscosity was explored by incorporating glycerol, yielding a maximal viscosity of 10.95 mPa·s. Full article
(This article belongs to the Special Issue Recent Advances in Advanced Laser Processing Technologies)
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<p>Photographs of (<b>a</b>) DI water with SiC target before PLAL and (<b>b</b>) after 5 min PLA; a set of samples produced at a constant PRR of 50 kHz; a scanning speed of 3 m/s; and laser powers of (<b>c</b>) 0.743, (<b>d</b>) 1.282, and (<b>e</b>) 1.504 W.</p>
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<p>UV-Vis measurements for the samples with varying laser processing parameters of (<b>a</b>) laser power, (<b>b</b>) scanning speed, and (<b>c</b>) pulse repletion rate (PRR). In each graph two other variables are kept constant and one variable changes.</p>
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<p>FTIR spectra of the target material and the produced NPs.</p>
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<p>DLS mass-weighted hydrodynamic diameters measurement for the samples with varying laser processing parameters of (<b>a</b>) PRR, (<b>b</b>) laser power, and (<b>c</b>) scanning speed. In each graph, two other variables were kept constant, and one variable changed.</p>
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<p>The DLS data illustrate the change in NPs’ mean diameter sizes with changing (<b>a</b>) laser power, (<b>b</b>) scanning speed, and (<b>c</b>) PRR.</p>
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<p>Dynamic light scattering mass-weighted hydrodynamic diameter patterns in a size range of up to 450 nm for a set of samples with laser powers of (<b>a</b>) 0.743 W, (<b>b</b>) 1.282, and (<b>c</b>) 1.505 W.</p>
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<p>The NPs’ concentration measurement as a function of (<b>a</b>) scanning speed, (<b>b</b>) PRR, and (<b>c</b>) laser power.</p>
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<p>FESEM images of produced SiC NPs: (<b>a</b>,<b>d</b>,<b>e</b>) SE acceleration voltage 1 kV, (<b>c</b>,<b>f</b>) SE acceleration voltage 15 kV, (<b>b</b>,<b>g</b>) SE acceleration voltage 10 kV, (<b>i</b>,<b>j</b>,<b>l</b>) SE acceleration voltage 20 kV, and (<b>h</b>,<b>k</b>) bright-field STEM acceleration voltage 10 kV and 20 kV, respectively.</p>
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<p>The EDX result and elemental mapping of the (<b>a</b>) SiC target material and (<b>b</b>) resulting NPs.</p>
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<p>Weight percentages of the elements observed in the EDX for the (<b>a</b>) target material and (<b>b</b>) produced NPs.</p>
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<p>Dynamic viscosity measurements at 25 °C as a function of the volumetric concentration of (<b>a</b>) acetone, (<b>b</b>) IPA, and (<b>c</b>) glycerol.</p>
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31 pages, 15968 KiB  
Article
Study on the Bond Performance of Epoxy Resin Concrete with Steel Reinforcement
by Peiqi Chen, Yueqiang Li, Xiaojie Zhou, Hao Wang and Jie Li
Buildings 2024, 14(9), 2905; https://doi.org/10.3390/buildings14092905 (registering DOI) - 14 Sep 2024
Viewed by 184
Abstract
Abstract: Epoxy resin concrete, characterized by its superior mechanical properties, is frequently utilized for structural reinforcement and strengthening. However, its application in structural members remains limited. In this paper, the bond–slip behavior between steel reinforcement and epoxy resin concrete was investigated using a [...] Read more.
Abstract: Epoxy resin concrete, characterized by its superior mechanical properties, is frequently utilized for structural reinforcement and strengthening. However, its application in structural members remains limited. In this paper, the bond–slip behavior between steel reinforcement and epoxy resin concrete was investigated using a combination of experimental research and finite element analysis, with the objective of providing data support for substantiating the expanded use of epoxy resin concrete in structural members. The research methodology included 18 center-pullout tests and 14 finite element model calculations, focusing on the effects of variables such as epoxy resin concrete strength, steel reinforcement strength, steel reinforcement diameter and protective layer thickness on bond performance. The results reveal that the bond strength between epoxy resin concrete and steel reinforcement significantly surpasses that of ordinary concrete, being approximately 3.23 times higher given the equivalent strength level of the material; the improvement in the strength of both the epoxy resin concrete and steel reinforcement are observed to marginally increase the bond stress. Conversely, an increase in the diameter of the steel reinforcement and a reduction in the thickness of the protective layer of the concrete can lead to diminished bond stress and peak slip. Particularly, when the steel reinforcement strength is below 500 MPa, it tends to reach its yield strength and may even detach during the drawing process, indicating that the yielding of the steel reinforcement occurs before the loss of bond stress. In contrast, for a steel reinforcement strength exceeding 500 MPa, yielding does not precede bond stress loss, resulting in a distinct form of failure described as scraping plough type destruction. Compared to ordinary concrete, the peak of the epoxy resin concrete and steel reinforcement bond stress–slip curve is more pointed, indicating a rapid degradation to maximum bond stress and exhibiting a brittle nature. Overall, these peaks are sharper than those of ordinary concrete, indicating a rapid decline in bond stress post-peak, reflective of its brittle characteristics. Full article
17 pages, 4195 KiB  
Article
Utilization of Tunnel Waste Slag for Cement-Stabilized Base Layers in Highway Engineering
by Junshuang Deng, Yongsheng Yao and Chao Huang
Materials 2024, 17(18), 4525; https://doi.org/10.3390/ma17184525 (registering DOI) - 14 Sep 2024
Viewed by 205
Abstract
The rapid expansion of highway infrastructure in the mountainous regions of China has led to a significant increase in tunnel construction, generating substantial amounts of tunnel waste slag. Concurrently, the development of transportation infrastructure has created a critical shortage of natural aggregates, necessitating [...] Read more.
The rapid expansion of highway infrastructure in the mountainous regions of China has led to a significant increase in tunnel construction, generating substantial amounts of tunnel waste slag. Concurrently, the development of transportation infrastructure has created a critical shortage of natural aggregates, necessitating the exploration of alternative sustainable sources. This study aimed to conduct a comprehensive evaluation of the physical and mechanical properties of tunnel waste slag and explore its potential for utilization in cement-stabilized base courses for highway engineering applications. The uniaxial compressive strength of the parent rock (tunnel waste slag) ranged from 81 MPa to 89 MPa in the desiccated state, indicating its suitability for use as a construction material. This study also determined the maximum dry density (2.432 g/cm3) and optimal moisture content (5.4%) of cement-stabilized mixtures incorporating recycled aggregates derived from tunnel waste slag. The splitting tensile strength of these mixtures at 28 days varied from 0.48 MPa to 0.73 MPa, demonstrating robust mechanical performance. Moreover, the unconfined compressive strength of these mixtures escalated from 7.0 MPa at 7 days to 11.0 MPa at 90 days, signifying a substantial enhancement in strength over time. These results validate the viability of utilizing tunnel waste slag in highway engineering and furnish valuable insights for designers, concrete manufacturers, and construction firms engaged in the development of cement-stabilized aggregate base courses. Full article
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Figure 1
<p>Characteristics of the gneiss rock sample: (<b>a</b>) apparent image and (<b>b</b>) XRD pattern.</p>
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<p>Grading curve of cement-stabilized crushed stone.</p>
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<p>Devices of the tunnel waste slag crushing process: (<b>a</b>) jaw crusher; (<b>b</b>) impact crusher.</p>
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<p>Schematic diagram of the single-axis compression tester.</p>
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<p>Schematic diagram of the unconfined compression tester.</p>
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<p>Uniaxial compressive strengths of the tunnel waste slag parent rock samples.</p>
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<p>Ultrasonic wave velocities of the tunnel waste slag parent rock samples.</p>
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<p>Main frequency amplitudes of the tunnel waste slag parent rock samples.</p>
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<p>Relationship between ultrasonic wave velocity and saturated compressive strength.</p>
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<p>Normal distribution prediction results for three shape parameters: (<b>a</b>) aspect, (<b>b</b>) roughness, and (<b>c</b>) angularity.</p>
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<p>Relationships between cement content and unconfined compressive strength.</p>
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<p>Unconfined compressive strengths of cement-stabilized crushed stone from different sampling locations.</p>
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<p>Splitting tensile strength of cement-stabilized crushed stone from different sampling locations.</p>
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<p>Correlation heat map of the strength characteristics of cement-stabilized crushed stone.</p>
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