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12 pages, 3203 KiB  
Article
Comparative Study of Electrospun Polydimethylsiloxane Fibers as a Substitute for Fluorine-Based Polymeric Coatings for Hydrophobic and Icephobic Applications
by Adrián Vicente, Pedro J. Rivero, Cleis Santos, Nadine Rehfeld and Rafael Rodríguez
Polymers 2024, 16(23), 3386; https://doi.org/10.3390/polym16233386 - 30 Nov 2024
Viewed by 500
Abstract
The development of superhydrophobic, waterproof, and breathable membranes, as well as icephobic surfaces, has attracted growing interest. Fluorinated polymers like PTFE or PVDF are highly effective, and previous research by the authors has shown that combining these polymers with electrospinning-induced roughness enhances their [...] Read more.
The development of superhydrophobic, waterproof, and breathable membranes, as well as icephobic surfaces, has attracted growing interest. Fluorinated polymers like PTFE or PVDF are highly effective, and previous research by the authors has shown that combining these polymers with electrospinning-induced roughness enhances their hydro- and ice-phobicity. The infusion of these electrospun mats with lubricant oil further improves their icephobic properties, achieving a slippery liquid-infused porous surface (SLIPS). However, their environmental impact has motivated the search for fluorine-free alternatives. This study explores polydimethylsiloxane (PDMS) as an ideal candidate because of its intrinsic properties, such as low surface energy and high flexibility, even at very low temperatures. While some published results have considered this polymer for icephobic applications, in this work, the electrospinning technique has been used for the first time for the fabrication of 95% pure PDMS fibers to obtain hydrophobic porous coatings as well as breathable and waterproof membranes. Moreover, the properties of PDMS made it difficult to process, but these limitations were overcome by adding a very small amount of polyethylene oxide (PEO) followed by a heat treatment process that provides a mat of uniform fibers. The experimental results for the PDMS porous coating confirm a hydrophobic behavior with a water contact angle (WCA) ≈ 118° and roll-off angle (αroll-off) ≈ 55°. In addition, the permeability properties of the fibrous PDMS membrane show a high transmission rate (WVD) ≈ 51.58 g∙m−2∙d−1, providing breathability and waterproofing. Finally, an ice adhesion centrifuge test showed a low ice adhesion value of 46 kPa. These results highlight the potential of PDMS for effective icephobic and waterproof applications. Full article
(This article belongs to the Section Polymer Fibers)
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<p>Schematic illustration of the fabrication methods used to produce F(PDMS) and F(SLIPS) samples through the following steps: (<b>i</b>) electrospinning corresponding to PEO-PDMS fibrous coating and HT<sub>0</sub>; (<b>ii</b>) membrane cleaning + silicon oil infusion.</p>
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<p>Scanning electron microscopy (SEM) images of the sample surface morphology F(PDMS) before (<b>a</b>) and after (<b>b</b>) thermal treatment.</p>
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<p>Histograms of the diameter distribution (<b>a</b>) and particle size (<b>b</b>) of the fiber sample F(PDMS).</p>
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<p>TGA curve of PDMS-PEO composite fibers with a weight ratio of 95:5.</p>
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<p>ATR-FTIR spectra of the samples F(PDMS) and PEO.</p>
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<p>Ice adhesion centrifuge test results for electrospun fibrous icephobic coatings and commercial references based on static ice formation.</p>
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17 pages, 9938 KiB  
Article
A Finite-Element-Based Investigation of the Influence of the Production Environment on Fuel Cell Membrane Electrode Assemblies During Manufacturing
by Ling Ma, Zhuoqi Yan, Sebastian Schabel and Jürgen Fleischer
Energies 2024, 17(22), 5737; https://doi.org/10.3390/en17225737 - 16 Nov 2024
Viewed by 448
Abstract
The manufacturing process for membrane electrode assemblies (MEAs), from coating to stack assembly, is typically performed under climate-controlled conditions due to the hygroscopic properties of catalyst-coated membranes (CCMs). Large climate-controlled areas in the assembly line not only increase the energy consumption but also [...] Read more.
The manufacturing process for membrane electrode assemblies (MEAs), from coating to stack assembly, is typically performed under climate-controlled conditions due to the hygroscopic properties of catalyst-coated membranes (CCMs). Large climate-controlled areas in the assembly line not only increase the energy consumption but also limit the scalability of the production line. In this study, experiments were conducted to analyze the effects of ambient humidity on the mechanical properties of a CCM. The hygroscopic swelling behavior of a commercial CCM with an ePTFE-reinforced membrane was also characterized. Using the finite element method, a 3D numerical model covering the entire MEA assembly process was developed, allowing for a numerical investigation of different climate control strategies. The influence of ambient humidity on the dimensional changes in the CCM, which leads to significant stress on the CCM due to mechanical constraints and thus to deformation of the MEA product, was simulated and validated experimentally using optical measurements. Finally, the critical steps during MEA assembly were identified, and a recommendation for the optimal humidity range for climate control was derived. Full article
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<p>Membrane tensile test setup.</p>
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<p>(<b>a</b>) Curves for strain and humidity with time variation during the experiment; (<b>b</b>) the curve of the first derivative of strain with time variation.</p>
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<p>Stress–strain curves for CCM at different humidity levels: (<b>a</b>) MD; (<b>b</b>) TD.</p>
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<p>Definition of the secant modulus and the proportional limit stress (50% RH, MD).</p>
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<p>Dimensional change as a function of relative humidity at various humidities.</p>
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<p>Hygroscopic expansion coefficient at different humidity levels and the fitted curve.</p>
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<p>Schematic views of the MEA design (<b>a</b>) 3D illustration; (<b>b</b>) cross-section (not true to scale).</p>
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<p>RH variation experiment for 4-layer MEA.</p>
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<p>Comparison of experimental and finite element simulation results for out-of-plane displacement of the CCM. (<b>a</b>) 50%-60%-75% humidity in X-direction; (<b>b</b>) 50%-60%-75% humidity in Y-direction; (<b>c</b>) 50%-40%-25% humidity in X-direction; and (<b>d</b>) 50%-40%-25% humidity in Y-direction.</p>
Full article ">Figure 9 Cont.
<p>Comparison of experimental and finite element simulation results for out-of-plane displacement of the CCM. (<b>a</b>) 50%-60%-75% humidity in X-direction; (<b>b</b>) 50%-60%-75% humidity in Y-direction; (<b>c</b>) 50%-40%-25% humidity in X-direction; and (<b>d</b>) 50%-40%-25% humidity in Y-direction.</p>
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<p>Von Mises stress states of the CCM and stress distribution along the middle path under humidity changes: (<b>a</b>) hydration cycle and (<b>b</b>) dehydration cycle.</p>
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<p>Stress variations in the upper GDL and the subgasket under different humidity cycles.</p>
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<p>The cross-sectional shape of the MEA in the Y-direction when the MEA returns to the initial humidity.</p>
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<p>The maximum in-plane stress of the CCM at different steps: (<b>a</b>) hydration and (<b>b</b>) dehydration.</p>
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<p>Deformation of MEA during hydration and dehydration in Y-direction: (<b>a</b>) RH: 50%-75% and (<b>b</b>) RH: 50%-25%.</p>
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<p>Cross-sectional shapes of five-layer MEA during different humidity changes.</p>
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<p>Schematic diagram explaining the deformation of the MEA after different humidity changes. (<b>a</b>) RH: 50-60-50-50 (%); (<b>b</b>) RH: 50-40-50-50 (%); and (<b>c</b>) RH: 50-50-40-50 (%).</p>
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<p>Schematic diagram explaining the deformation of the MEA after different humidity changes. (<b>a</b>) RH: 50-60-50-50 (%); (<b>b</b>) RH: 50-40-50-50 (%); and (<b>c</b>) RH: 50-50-40-50 (%).</p>
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13 pages, 5714 KiB  
Article
Fabrication and Tribology Properties of PTFE-Coated Cemented Carbide Under Dry Friction Conditions
by Shoujun Wang, Wenlong Song, Lei An, Zixiang Xia and Shengdong Zhang
Lubricants 2024, 12(11), 363; https://doi.org/10.3390/lubricants12110363 - 23 Oct 2024
Cited by 1 | Viewed by 541
Abstract
PTFE coatings were deposited on YT15 carbide substrates using spray technology. A series of examinations were conducted, including the use of surface and cross-section micrographs to analyze the structural integrity of the coatings. The surface roughness, the adhesion force between the PTFE coatings [...] Read more.
PTFE coatings were deposited on YT15 carbide substrates using spray technology. A series of examinations were conducted, including the use of surface and cross-section micrographs to analyze the structural integrity of the coatings. The surface roughness, the adhesion force between the PTFE coatings and the carbide substrate, and the micro-hardness of the coated carbide were also evaluated. Additionally, the friction and wear behaviors were assessed through dry sliding friction tests against WC/Co balls. The test results indicated that while the PTFE-coated carbide exhibited a rougher surface and reduced micro-hardness, it also demonstrated a significant reduction in surface friction and adhesive wear. These findings suggest that the PTFE coatings enhance the overall wear resistance of the carbides. The lower surface hardness and shear strength of the coatings influenced the friction performance, leading to specific wear failure mechanisms, such as abrasion wear, coating delamination, and flaking. Overall, the deposition of PTFE coatings on carbide substrates presents a promising strategy to enhance their friction and wear performance. This approach not only improves the durability of carbide materials but also offers potential applications in industries where reduced friction and wear are critical for performance. Full article
(This article belongs to the Special Issue Tribological Properties of Sprayed Coatings)
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<p>Optical images of the uncoated specimen (<b>a</b>) and the coated specimen (<b>b</b>).</p>
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<p>SEM micrographs (<b>a</b>,<b>b</b>), EDS element analyses of points A (<b>c</b>) and B (<b>d</b>) in (<b>b</b>), and cross-section micrograph (<b>e</b>) of the coated specimen.</p>
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<p>The 3D topographies of specimens without (<b>a</b>) and with coatings (<b>b</b>), obtained by a white light interferometer.</p>
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<p>Scratch curve of the coated specimen.</p>
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<p>Scratch micrographs (<b>a</b>,<b>b</b>) and EDS element analysis results for points A (<b>c</b>) and B (<b>d</b>) in (<b>a</b>).</p>
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<p>Scratch micrographs (<b>a</b>,<b>b</b>) and EDS element analysis results for points A (<b>c</b>) and B (<b>d</b>) in (<b>a</b>).</p>
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<p>Nanoindentation load-displacement curves of the PTFE-coated carbide.</p>
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<p>Friction coefficient curves under different loads during 15 min friction tests (sliding speed = 8 mm/s): (<b>a</b>) 20 N; (<b>b</b>) 40 N; (<b>c</b>) 60 N; (<b>d</b>) 80 N.</p>
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<p>Friction coefficient curves at different sliding speeds during 15 min friction tests (load = 60 N): (<b>a</b>) 4 mm/s; (<b>b</b>) 6 mm/s; (<b>c</b>) 8 mm/s; (<b>d</b>) 10 mm/s.</p>
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<p>SEM micrographs (<b>a</b>,<b>b</b>) and EDS composition analysis at points A and B (<b>c</b>,<b>d</b>) in the worn surface for the uncoated specimen after the 15 min friction test (load = 60 N, sliding speed = 8 mm/s).</p>
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<p>SEM micrographs (<b>a</b>,<b>b</b>,<b>e</b>) and EDS composition analysis result for points A and B (<b>c</b>,<b>d</b>) in the worn surface for the coated specimen after the 15 min friction test (load = 60 N, sliding speed = 8 mm/s).</p>
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18 pages, 691 KiB  
Systematic Review
Coating Materials to Prevent Screw Loosening in Single Dental Implant Crowns: A Systematic Review
by Lara Coelho, Maria-Cristina Manzanares-Céspedes, Joana Mendes, Victòria Tallón-Walton, Wilson Astudillo-Rozas, Carlos Aroso and José Manuel Mendes
Materials 2024, 17(20), 5053; https://doi.org/10.3390/ma17205053 - 16 Oct 2024
Viewed by 755
Abstract
Oral rehabilitation with dental implants has resulted in high success rates. However, some complications have been described, such as the loss of the prosthetic screw. Some manufacturers sell screws with different coatings to avoid screw loosening, but even these types of screws can [...] Read more.
Oral rehabilitation with dental implants has resulted in high success rates. However, some complications have been described, such as the loss of the prosthetic screw. Some manufacturers sell screws with different coatings to avoid screw loosening, but even these types of screws can come loose. We aimed to investigate the screw coatings that can be applied during a dental appointment to avoid screw loosening. Following PRISMA Guidelines, we searched PubMed/Medline, Embase and Web of Science for studies published up to January 2024. All studies of single dental implant crowns, in which the prosthetic screw was coated with a lubricant and the preload and/or the removal torque value (RTV) was recorded, were analyzed. We excluded studies applying the finite element method (FEM) as well as studies without a control group. The risk of bias was assessed with a tool developed by our research group. Of the 1959 records identified, 19 were selected. Ten studies were considered to have a low risk of bias, and nine were considered to have a medium risk of bias. The coatings tested were adhesives, saliva, chlorhexidine, Vaseline, silicone gel, Polytetrafluoroethylene (PTFE) tape, blood, fluoride, Listerine® Mouthwash and normal saline. The preload, the RTV with and without cyclic loading and the percentage of RTV loss were recorded. Some coatings show promise, although there is no clear evidence that any option is superior in minimizing screw loosening. Full article
(This article belongs to the Special Issue Biomaterials for Restorative Dentistry)
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<p>Flowchart of the screening process (PRISMA format).</p>
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16 pages, 6813 KiB  
Article
Study on the Wear Performance of Surface Alloy Coating of Inner Lining Pipe under Different Load and Mineralization Conditions
by Yuntao Xi, Yucong Bi, Yang Wang, Lan Wang, Shikai Su, Lei Wang, Liqin Ding, Shanna Xu, Haitao Liu, Xinke Xiao, Ruifan Liu and Jiangtao Ji
Coatings 2024, 14(10), 1274; https://doi.org/10.3390/coatings14101274 - 4 Oct 2024
Viewed by 841
Abstract
Testing was carried out in this study to evaluate the friction and wear performance of 45# steel inner liner pipes with cladding, along with four different types of centralizing materials (45# steel, nylon, polytetrafluoroethylene (PTFE), and surface alloy coating) in oil field conditions. [...] Read more.
Testing was carried out in this study to evaluate the friction and wear performance of 45# steel inner liner pipes with cladding, along with four different types of centralizing materials (45# steel, nylon, polytetrafluoroethylene (PTFE), and surface alloy coating) in oil field conditions. Under dry-friction conditions, the coefficients of friction and rates of wear are significantly higher than their counterparts in aqueous solutions. This is attributed to the lubricating effect provided by the aqueous solution, which reduces direct friction between contact surfaces, thereby lowering wear. As the degree of mineralization in the aqueous solution increases, the coefficient of friction tends to decrease, indicating that an elevated level of mineralization enhances the lubricating properties of the aqueous solution. The wear pattern in an aqueous solution is similar to that in dry-friction conditions under different loads, but with a lower friction coefficient and wear rate. The coating has played an important role in protecting the wear process of 45# steel, and the friction coefficient and wear rate of tubing materials under various environmental media have been significantly reduced. In terms of test load, taking into account the friction coefficient and wear rate, the suggested order for centralizing materials for lining oil pipes with the surface alloy coating is as follows: (i) surface alloy coating, (ii) nylon, (iii) PTFE, and (iv) 45# steel. Full article
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Figure 1
<p>Pin disc friction and wear experimental device: (<b>a</b>) schematic diagram, (<b>b</b>) physical image, and (<b>c</b>) control interface; mineralization degree aqueous solution environmental device: (<b>d</b>) schematic diagram and (<b>e</b>) physical image.</p>
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<p>Pin disc friction and wear experimental device: (<b>a</b>) schematic diagram, (<b>b</b>) physical image, and (<b>c</b>) control interface; mineralization degree aqueous solution environmental device: (<b>d</b>) schematic diagram and (<b>e</b>) physical image.</p>
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<p>Friction coefficient of surface alloy coating of inner lining tubing material under different mineralization degrees: (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with mineralization degree; variation in wear rate with different degrees of mineralization: (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
Full article ">Figure 2 Cont.
<p>Friction coefficient of surface alloy coating of inner lining tubing material under different mineralization degrees: (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with mineralization degree; variation in wear rate with different degrees of mineralization: (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
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<p>Friction coefficient of surface-alloy-coating-lined oil pipe material under different test loads (dry friction): (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with applied load (dry friction); variation in wear rate with applied load (dry friction): (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
Full article ">Figure 3 Cont.
<p>Friction coefficient of surface-alloy-coating-lined oil pipe material under different test loads (dry friction): (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with applied load (dry friction); variation in wear rate with applied load (dry friction): (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
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<p>Friction coefficient of surface-alloy-coating-lined oil pipe material under different test loads (aqueous solution): (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with applied load; variation in wear rate with applied load (30,000 mg/L mineralization-degree aqueous solution): (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
Full article ">Figure 4 Cont.
<p>Friction coefficient of surface-alloy-coating-lined oil pipe material under different test loads (aqueous solution): (<b>a</b>) cladded 45# steel inner liner pipes (disc)–45# steel (pin), (<b>b</b>) cladded 45# steel inner liner pipes (disc)–nylon (pin), (<b>c</b>) cladded 45# steel inner liner pipes (disc)–PTFE (pin), and (<b>d</b>) cladded 45# steel inner liner pipes (disc)–surface alloy coating (pin); (<b>e</b>) variation in friction coefficient of cladded 45# steel inner liner pipes with applied load; variation in wear rate with applied load (30,000 mg/L mineralization-degree aqueous solution): (<b>f</b>) oil pipe material and (<b>g</b>) centralizing material.</p>
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<p>SEM images of the worn surface of cladded 45# steel inner liner pipes (disc)–PTFE (pin) under different loading conditions in a 30,000 mg/L mineralization-degree aqueous solution: (<b>a</b>) cladded 45# steel inner liner pipes under 50 N, (<b>b</b>) PTFE under 50 N, (<b>c</b>) cladded 45# steel inner liner pipes under 500 N, (<b>d</b>) PTFE under 500 N, (<b>e</b>) cladded 45# steel inner liner pipes under 1000 N, (<b>f</b>) PTFE under 1000 N, (<b>g</b>) cladded 45# steel inner liner pipes under 2000 N, and (<b>h</b>) PTFE under 2000 N.</p>
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<p>Three-dimensional confocal microscopic images and height contour of cladded 45# steel inner liner pipes (disc)–PTFE (pin) under different loading conditions in a 30,000 mg/L mineralization-degree aqueous solution: (<b>a</b>) cladded 45# steel inner liner pipes under 50 N, (<b>b</b>) cladded 45# steel inner liner pipes under 500 N, (<b>c</b>) cladded 45# steel inner liner pipes 1000 N, (<b>d</b>) cladded 45# steel inner liner pipes under 2000 N, (<b>e</b>) PTFE under 50 N, (<b>f</b>) PTFE under 500 N, (<b>g</b>) PTFE under 500 N, (<b>h</b>) PTFE under 1000 N.</p>
Full article ">Figure 6 Cont.
<p>Three-dimensional confocal microscopic images and height contour of cladded 45# steel inner liner pipes (disc)–PTFE (pin) under different loading conditions in a 30,000 mg/L mineralization-degree aqueous solution: (<b>a</b>) cladded 45# steel inner liner pipes under 50 N, (<b>b</b>) cladded 45# steel inner liner pipes under 500 N, (<b>c</b>) cladded 45# steel inner liner pipes 1000 N, (<b>d</b>) cladded 45# steel inner liner pipes under 2000 N, (<b>e</b>) PTFE under 50 N, (<b>f</b>) PTFE under 500 N, (<b>g</b>) PTFE under 500 N, (<b>h</b>) PTFE under 1000 N.</p>
Full article ">Figure 6 Cont.
<p>Three-dimensional confocal microscopic images and height contour of cladded 45# steel inner liner pipes (disc)–PTFE (pin) under different loading conditions in a 30,000 mg/L mineralization-degree aqueous solution: (<b>a</b>) cladded 45# steel inner liner pipes under 50 N, (<b>b</b>) cladded 45# steel inner liner pipes under 500 N, (<b>c</b>) cladded 45# steel inner liner pipes 1000 N, (<b>d</b>) cladded 45# steel inner liner pipes under 2000 N, (<b>e</b>) PTFE under 50 N, (<b>f</b>) PTFE under 500 N, (<b>g</b>) PTFE under 500 N, (<b>h</b>) PTFE under 1000 N.</p>
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10 pages, 3088 KiB  
Article
Solvent-Free Method of Polyacrylonitrile-Coated LLZTO Solid-State Electrolytes for Lithium Batteries
by Xuehan Wang, Kaiqi Zhang, Huilin Shen, Hao Zhang, Hongyan Yao, Zheng Chen and Zhenhua Jiang
Molecules 2024, 29(18), 4452; https://doi.org/10.3390/molecules29184452 - 19 Sep 2024
Viewed by 791
Abstract
Solid-state electrolytes (SSEs), particularly garnet-type Li6.4La3Zr1.4Ta0.6O12 (LLZTO), offer high stability and a wide electrochemical window. However, their grain boundaries limit ionic conductivity, necessitating high-temperature sintering for improved performance. Yet, this process results in brittle [...] Read more.
Solid-state electrolytes (SSEs), particularly garnet-type Li6.4La3Zr1.4Ta0.6O12 (LLZTO), offer high stability and a wide electrochemical window. However, their grain boundaries limit ionic conductivity, necessitating high-temperature sintering for improved performance. Yet, this process results in brittle electrolytes prone to fracture during manufacturing. To address these difficulties, solvent-free solid-state electrolytes with a polyacrylonitrile (PAN) coating on LLZTO particles are reported in this work. Most notably, the PAN-coated LLZTO (PAN@LLZTO) electrolyte demonstrates self-supporting characteristics, eliminating the need for high-temperature sintering. Importantly, the homogeneous polymeric PAN coating, synthesized via the described method, facilitates efficient Li+ transport between LLZTO particles. This electrolyte not only achieves an ionic conductivity of up to 2.11 × 10−3 S cm−1 but also exhibits excellent interfacial compatibility with lithium. Furthermore, a lithium metal battery incorporating 3% PAN@LLZTO-3%PTFE as the solid-state electrolyte and LiFePO4 as the cathode demonstrates a remarkable specific discharge capacity of 169 mAh g−1 at 0.1 °C. The strategy of organic polymer-coated LLZTO provides the possibility of a green manufacturing process for preparing room-temperature sinter-free solid-state electrolytes, which shows significant cost-effectiveness. Full article
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<p>(<b>a</b>) Synthesis of 3% PAN@LLZTO composite electrolyte powder; SEM images: (<b>b</b>) LLZTO powder and (<b>c</b>) 3% PAN@LLZTO powder; (<b>d</b>) XRD image and (<b>e</b>) FT-IR spectra of PAN, LLZTO, and 3% PAN@LLZTO.</p>
Full article ">Figure 2
<p>(<b>a</b>) Synthesis of 3% PAN@LLZTO-PTFE membranes; SEM of: (<b>b</b>) the mixture of 3% PAN@LLZTO and PTFE, (<b>c</b>) 3% PAN@LLZTO powder and micro-fibrillated PTFE flocculent, (<b>d</b>) enhanced fibrillation of the flocculent structure, (<b>e</b>) total fibrillating of the 3% PAN@LLZTO-PTFE; SEM of 3% PAN@LLZTO-PTFE calendaring after: (<b>f</b>) 5 times; (<b>g</b>) 10 times; (<b>h</b>) 15 times; (<b>i</b>) 20 times; Variation of (<b>j</b>) tensile strength with the number of calendaring cycles, (<b>k</b>) tensile strength with electrolyte film thickness, and (<b>l</b>) ionic conductivity with PTFE content; (<b>m</b>) factors influencing the fibrillation degree of solvent-free SSE films.</p>
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<p>(<b>a</b>) Thickness measurement diagram and schematic diagram for cutting 16mm diameter of 3% PAN@LLZTO-3%PTFE; (<b>b</b>) impedance of LLZTO-3%PTFE and 3% PAN@LLZTO-3%PTFE; (<b>c</b>) linear scanning voltammetry of 3% PAN@LLZTO-3%PTFE; (<b>d</b>) Li plating/stripping curves of LLZTO-3%PTFE and 3% PAN@LLZTO-3%PTFE.</p>
Full article ">Figure 4
<p>Electrochemical properties of LFP|3% PAN@LLZTO-3%PTFE|Li batteries. (<b>a</b>) Battery’s structure diagram; (<b>b</b>) impedance before and after cycle; (<b>c</b>) Coulombic efficiency during the three cycles; (<b>d</b>) discharge rate curves at 0.1 °C, 0.2 °C, 0.3 °C, 0.5 °C, 1.0 °C; (<b>e</b>) charge and discharge voltage profiles obtained at different cycles; (<b>f</b>) long-term cycling performance at 0.1 °C compared with LFP|LLZTO-3%PTFE|Li.</p>
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16 pages, 2201 KiB  
Article
Hydrogen Generation by Nickel Electrodes Coated with Linear Patterns of PTFE
by Alion Alushi, Atheer Al-Musawi, Kyuman Kim, Chong-Yong Lee, Klaudia Wagner and Gerhard F. Swiegers
J. Compos. Sci. 2024, 8(9), 368; https://doi.org/10.3390/jcs8090368 - 19 Sep 2024
Viewed by 841
Abstract
Previous studies have shown that partially coating electrode surfaces with patterns of ‘islands’ of hydrophobic tetrafluoroethylene (PTFE; Teflon) may lead to more energy efficient gas generation. This occurred because the gas bubbles formed preferentially on the PTFE, thereby freeing up the catalytically active [...] Read more.
Previous studies have shown that partially coating electrode surfaces with patterns of ‘islands’ of hydrophobic tetrafluoroethylene (PTFE; Teflon) may lead to more energy efficient gas generation. This occurred because the gas bubbles formed preferentially on the PTFE, thereby freeing up the catalytically active metallic surfaces to produce the gas more efficiently. This work examined electrochemically induced hydrogen bubble formation on a nickel electrode surface that had been coated with linear patterns of PTFE. The impact of the PTFE line size (width) and degree of coverage was examined and analyzed. No improvement in electrical energy efficiency was observed up to 15 mA/cm2 when comparing the PTFE-coated electrodes with the control bare uncoated electrode. However, increasing PTFE coverage up to 15% generally improved electrolysis performance. Moreover, samples with 50% wider lines performed better (at the equivalent PTFE coverage), yielding an overpotential decline of up to 3.9% depending on the PTFE coverage. A ‘bubble-scavenging’ phenomenon was also observed, wherein bubbles present on the PTFE lines rapidly shrunk until they disappeared. Full article
(This article belongs to the Special Issue Advancements in Composite Materials for Energy Storage Applications)
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<p>Concentration of oxygen (blue) and bubble radius (red). Bubble nucleates (r &gt; 0) when gas has reached nucleation concentration. Reproduced with permission from [<a href="#B23-jcs-08-00368" class="html-bibr">23</a>].</p>
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<p>Schematic view of vertically positioned electrode with bubble attached (dashed-line circle) and released bubble (full-line circle) after some time. After the bubble reaches detachment size, it detaches due to buoyancy forces overcoming adhering forces. Produced according to [<a href="#B23-jcs-08-00368" class="html-bibr">23</a>,<a href="#B26-jcs-08-00368" class="html-bibr">26</a>].</p>
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<p>Schematic depiction of a water droplet on a hydrophilic/aerophobic surface with contact angle θ &lt; 90° (<b>left</b>) and a hydrophobic/aerophilic surface with contact angle θ &gt; 90° (<b>right</b>). Adapted and reproduced with permission from [<a href="#B29-jcs-08-00368" class="html-bibr">29</a>].</p>
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<p>Marangoni effect on a Ni electrode with a PTFE ‘island’ coated on it. Water molecules, which are hydrophilic, are repelled by and move away from PTFE to higher surface tension regions, while gas bubbles (or molecules), which are also hydrophobic, are attracted to and move toward the PTFE island. Reproduced referring to the theory described in [<a href="#B29-jcs-08-00368" class="html-bibr">29</a>,<a href="#B30-jcs-08-00368" class="html-bibr">30</a>].</p>
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<p>Results of milling machine engraving of 1.5 mm-wide lines, each with a depth of 0.34 mm. The lines were later filled with PTFE, given an electrode with PTFE lines upon its surface.</p>
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<p>A 3D laser microscope image of the electrode surface after the polishing procedure. Tiny scratches of nm thickness are visible.</p>
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<p>(<b>a</b>) PTFE-coated samples after heat treatment, showing the overall percentage of coverage with PTFE of the left; (<b>b</b>) control bare electrode sample after heat treatment.</p>
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<p>Photograph and image analysis (pixelation) to determine PTFE coverage using the program ImageJ. The photograph was adjusted until the PTFE line was filled with a red color, whereafter the ratio of red pixels to all pixels gave the PTFE coverage of the entire image.</p>
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<p>Schematic view of 3-electrode setup of the cell (WE, CE, REF). The WE–CE distance was 30 mm with the REF in the middle, placed 15 cm from each electrode.</p>
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<p>Electrochemical cell assembly.</p>
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<p>Snapshot of video recording during CP run on bare uncoated electrode at 15 mA/cm<sup>2</sup>.</p>
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<p>Image sequence (at 00:00:08 and 00:00:15 s) of CP run on 15%_1.5 mm sample. Bubble size grows.</p>
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<p>Image sequence (at 00:00:45 and 00:00:46 s) of CP run on 15%_1.5 mm sample. Even after reaching detachment size, the bubble does not detach completely but stays attached on the PTFE line and travels along the line toward the electrolyte surface.</p>
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<p>Bubble coalescence onto the PTFE line of two bubbles sitting at the PTFE–Ni interface at second 00:00:54 and 00:00:55 (marked with black circles).</p>
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<p>‘Bubble-scavenging’ effect of the coalesced bubble on PTFE at second 00:00:56 and 00:00:57 (marked with black circles). The bubble is assumed to ‘deflate’ due to gas being removed toward the water surface along the PTFE line.</p>
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<p>Polarization curves of samples coated with 1 mm PTFE lines (geometrical active area); CP.</p>
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<p>Polarization curves of samples coated with 1.5 mm PTFE lines (geometrical active area); CP.</p>
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13 pages, 12300 KiB  
Article
Preparation and Properties of Lightweight Amphiphobic Proppant for Hydraulic Fracturing
by Guang Wang, Qinyue Ma, Longqiang Ren and Jirui Hou
Polymers 2024, 16(18), 2575; https://doi.org/10.3390/polym16182575 - 12 Sep 2024
Viewed by 675
Abstract
The wettability of the proppant is crucial in optimizing the flowback of fracturing fluids and improving the recovery of the produced hydrocarbons. Neutral wet proppants have been proven to improve the fluid flow by reducing the interaction between the fluid and the proppant [...] Read more.
The wettability of the proppant is crucial in optimizing the flowback of fracturing fluids and improving the recovery of the produced hydrocarbons. Neutral wet proppants have been proven to improve the fluid flow by reducing the interaction between the fluid and the proppant surface. In this study, a lightweight amphiphobic proppant (LWAP) was prepared by coating a lightweight ceramic proppant (LWCP) with phenolic resin, epoxy resin, polytetrafluoroethylene (PTFE), and trimethoxy(1H,1H,2H,2H-heptadecafluorodecyl)silane (TMHFS) using a layer-by-layer method. The results indicated that the LWAP exhibited a breakage ratio of 2% under 52 MPa (7.5 K) closure stress, with an apparent density of 2.12 g/cm3 and a bulk density of 1.21 g/cm3. The contact angles of water and olive oil were 125° and 104°, respectively, changing to 124° and 96° after displacement by water and diesel oil. A comparison showed that the LWAP could transport over a significantly longer distance than the LWCP, with the length increasing by more than 80%. Meanwhile, the LWAP displayed notable resistance to scale deposition on the proppant surface compared to the LWCP. Furthermore, the maintained conductivity of the LWAP was higher than that of the LWCP after displacement by water and oil phases alternately. The modified proppant could minimize production declines during hydrocarbon extraction in unconventional reservoirs. Full article
(This article belongs to the Section Polymer Applications)
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<p>Schematics of the modification process.</p>
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<p>(<b>a</b>) Photograph of fracture model apparatus; (<b>b</b>) schematic of plexiglass fracture cell (not to scale).</p>
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<p>Optical and SEM images of proppants: (<b>a</b>,<b>c</b>) LWCP; (<b>b</b>,<b>d</b>) LWAP.</p>
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<p>(<b>a</b>) SEM images of various scales of LWAP grains; (<b>b</b>) images of liquid drops on LWAP; (<b>c</b>) images of water drop on LWAP; (<b>d</b>) images of olive oil drop on LWAP.</p>
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<p>Images of LWAP suspended on the surfaces of different liquids; (<b>a</b>) LWAP suspended on the surfaces of water; (<b>b</b>) LWAP suspended on the surfaces of silicone oil.</p>
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<p>Liquid drops on LWAP under displacement with water and oil; (<b>a</b>) images of liquid drops on LWAP; (<b>b</b>) images of water drop on LWAP; (<b>c</b>) images of olive oil drop on LWAP.</p>
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<p>Images of proppant placement in fracture systems and the state in water after stirring (2 ppm sodium dodecyl sulfate solution): (<b>a</b>) LWCP placement in fracture system; (<b>b</b>) LWAP placement in fracture system; (<b>c</b>,<b>d</b>) the state in water after stirring. (The blue lines in (<b>a</b>,<b>b</b>) are auxiliary curves representing the settled proppant bed heights; The red lines in (<b>a</b>,<b>b</b>) are auxiliary curves representing the settled proppant bed heights; The area between the right and middle red lines (<b>a</b>,<b>b</b>)represents the length of the LWCP settling bed, and the area between the right and left red lines (<b>a</b>,<b>b</b>) represents the length of the LWAP settling bed.).</p>
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<p>SEM images and EDX of proppant: LWCP (<b>a</b>,<b>b</b>); LWCP immersed in brine (<b>c</b>,<b>d</b>); LWAP immersed in brine (<b>e</b>,<b>f</b>). (The red boxes in (<b>a</b>,<b>c</b>,<b>e</b>) are the EDX spectral scanning sampling areas).</p>
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<p>Conductivity (<b>a</b>) and maintained conductivity under 40 MPa (<b>b</b>) of different proppants using DI water as a flowing fluid (LWCP1 and LWAP1 after water and oil displacement).</p>
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13 pages, 3670 KiB  
Article
Influence of Polytetrafluoroethylene Content, Compaction Pressure, and Annealing Treatment on the Magnetic Properties of Iron-Based Soft Magnetic Composites
by Mei Song, Fan Luo, Yajing Shang and Zhongxia Duan
Molecules 2024, 29(17), 4019; https://doi.org/10.3390/molecules29174019 - 25 Aug 2024
Viewed by 658
Abstract
To improve the magnetic properties of iron-based soft magnetic composites (SMCs), polytetrafluoroethylene (PTFE) with excellent heat resistance, electrical insulation, and extremely high electrical resistivity was chosen as an insulating coating material for the preparation of iron-based SMCs. The effects of PTFE content, compaction [...] Read more.
To improve the magnetic properties of iron-based soft magnetic composites (SMCs), polytetrafluoroethylene (PTFE) with excellent heat resistance, electrical insulation, and extremely high electrical resistivity was chosen as an insulating coating material for the preparation of iron-based SMCs. The effects of PTFE content, compaction pressure, and annealing treatment on the magnetic properties of Fe/PTFE SMCs were investigated in detail. The results demonstrate that the PTFE insulating layer is successfully coated on the surface of iron powders, which effectively reduces the core loss, increases the resistivity, and improves the frequency stability and the quality factor. Under the combined effect of optimal PTFE content, compaction pressure, and annealing treatment, the iron-based SMCs exhibit a high effective permeability of 56, high saturation magnetization of 192.9 emu/g, and low total core losses of 355 mW/cm3 and 1705 mW/cm3 at 50 kHz for Bm = 50 mT and 100 mT. This work provides a novel insulating coating layer that optimizes magnetic properties and is advantageous for the development of iron-based SMCs. In addition, it also provides a comprehensive understanding of the relationship between process parameters and magnetic properties, which is of great guiding significance for scientific research and industrial production. Full article
(This article belongs to the Special Issue Organometallic Compounds: Design, Synthesis and Application)
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<p>(<b>a</b>) SEM image of the raw iron powders; (<b>b</b>,<b>c</b>) are a partial enlargement corresponding to the red boxes in (<b>a</b>,<b>b</b>); (<b>d</b>) SEM image of the Fe/PTFE composite powders containing 3 wt% PTFE; (<b>e</b>,<b>f</b>) are a partial enlargement corresponding to the red boxes in (<b>d</b>,<b>e</b>).</p>
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<p>XRD patterns of the PTFE powders (black line), raw iron powders (red line), and Fe/PTFE composite powders containing 3 wt% PTFE (blue line).</p>
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<p>(<b>a</b>) SEM image of the cross-section of Fe/PTFE SMCs coated with 3 wt% PTFE; (<b>b</b>) is a partial enlargement corresponding to the white circle in (<b>a</b>); EDS spectra of (<b>c</b>) PTFE insulating layer and (<b>d</b>) iron particles for the Fe/PTFE SMCs coated with 3 wt% PTFE.</p>
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<p>(<b>a</b>) Effective permeability of Fe/PTFE SMCs as a function of PTFE contents at three different frequencies; (<b>b</b>) quality factor of Fe/PTFE SMCs with different PTFE contents versus frequency.</p>
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<p>(<b>a</b>) Saturation magnetization (black line) and coercivity (red line) of Fe/PTFE SMCs containing different PTFE contents at a magnetic field of 20,000 Oe; (<b>b</b>) total core loss of Fe/PTFE SMCs with different PTFE contents measured at 50 kHz for B<sub>m</sub> = 50 mT and 100 mT, respectively.</p>
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<p>(<b>a</b>) Effective permeability and (<b>b</b>) quality factor of Fe/PTFE SMCs containing 3 wt% PTFE with various compaction pressures versus frequency.</p>
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<p>(<b>a</b>,<b>b</b>) Total core loss as a function of frequency for the Fe/PTFE SMCs containing 3 wt% PTFE at different pressures measured at (<b>a</b>) B<sub>m</sub> = 50 mT and (<b>b</b>) 100 mT; (<b>c</b>) total core loss as a function of compaction pressure for the Fe/PTFE SMCs containing 3 wt% PTFE measured at 50 kHz for B<sub>m</sub> = 50 mT and 100 mT, respectively.</p>
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<p>(<b>a</b>) Effective permeability and (<b>b</b>) quality factor as a function of frequency for the Fe/PTFE SMCs containing 3 wt% PTFE annealed at different temperatures.</p>
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<p>(<b>a</b>,<b>b</b>) Total core loss as a function of frequency for the Fe/PTFE SMCs containing 3 wt% PTFE annealed at different temperatures measured at (<b>a</b>) B<sub>m</sub> = 50 mT and (<b>b</b>) 100 mT; (<b>c</b>) total core loss as a function of annealing temperature for the Fe/PTFE SMCs containing 3 wt% PTFE measured at 50 kHz for B<sub>m</sub> = 50 mT and 100 mT, respectively.</p>
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16 pages, 6386 KiB  
Article
Fouling Reduction and Thermal Efficiency Enhancement in Membrane Distillation Using a Bilayer-Fluorinated Alkyl Silane–Carbon Nanotube Membrane
by Sumona Paul, Mitun Chandra Bhoumick and Somenath Mitra
Membranes 2024, 14(7), 152; https://doi.org/10.3390/membranes14070152 - 10 Jul 2024
Cited by 1 | Viewed by 1402
Abstract
In this study, we report the robust hydrophobicity, lower fouling propensity, and high thermal efficiency of the 1H,1H,2H,2H-perfluorooctyltriethoxysilane (FAS)-coated, carbon nanotube-immobilized membrane (CNIM) when applied to desalination via membrane distillation. Referred to as FAS-CNIM, the membrane was developed through a process that combined [...] Read more.
In this study, we report the robust hydrophobicity, lower fouling propensity, and high thermal efficiency of the 1H,1H,2H,2H-perfluorooctyltriethoxysilane (FAS)-coated, carbon nanotube-immobilized membrane (CNIM) when applied to desalination via membrane distillation. Referred to as FAS-CNIM, the membrane was developed through a process that combined the drop-casting of nanotubes flowed by a dip coating of the FAS layer. The membranes were tested for porosity, surface morphology, thermal stability, contact angle, and flux. The static contact angle of the FAS-CNIM was 153 ± 1°, and the modified membrane showed enhancement in water flux by 18% compared to the base PTFE membrane. The flux was tested at different operating conditions and the fouling behavior was investigated under extreme conditions using a CaCO3 as well as a mixture of CaCO3 and CaSO4 solution. The FAS-CNIM showed significantly lower fouling than plain PTFE or the CNIM; the relative flux reduction was 34.4% and 37.6% lower than the control for the CaCO3 and CaCO3/CaSO4 mixed salt solution. The FAS-CNIM exhibited a notable decrease in specific energy consumption (SEC). Specifically, the SEC for the FAS-CNIM measured 311 kwh/m3 compared to 330.5 kwh/m3 for the CNIM and 354 kwh/m3 for PTFE using a mixture of CaCO3/CaSO4. This investigation underscores the significant contribution of the carbon nanotubes’ (CNTs) intermediate layer in creating a durable superhydrophobic membrane, highlighting the potential of utilizing carbon nanotubes for tailored interface engineering to tackle fouling for salt mixtures. The innovative design of a superhydrophobic membrane has the potential to alleviate wetting issues resulting from low surface energy contaminants present in the feed of membrane distillation processes. Full article
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<p>Structure of FAS-CNIM membrane.</p>
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<p>Experimental setup for SGMD.</p>
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<p>The contact angle of the PTFE, CNIM, and FAS-CNIM membranes.</p>
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<p>SEM images (<b>a</b>–<b>c</b>), Raman spectra (<b>d</b>), and thermogravimetric analysis of different membranes, namely PTFE, CNIM, and FAS-CNIM membranes (<b>e</b>).</p>
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<p>Membrane flux as a function of temperature for both a single salt (CaCO<sub>3</sub>, 2.8 g/L) and a mixture of salts (CaCO<sub>3</sub> 2.8 g/L and CaSO<sub>4</sub> 6.6 g/L) in the first hour of the SGMD study. The flow rate was maintained at 120 mL/min.</p>
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<p>The fouling of membranes by CaCO<sub>3</sub> at 80 °C for 16 h of the SGMD study. The flow rate was maintained at 120 mL/min.</p>
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<p>The fouling of membranes by CaCO<sub>3</sub>/CaSO<sub>4</sub> at 80 °C for 16 h of the SGMD study. The flow rate was maintained at 120 mL/min.</p>
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<p>SEM images of the salt deposition after 16 h over the membrane surface. (<b>a</b>). CaCO<sub>3</sub> salt deposition over the PTFE membrane surface. (<b>b</b>). CaCO<sub>3</sub> salt deposition on the CNIM surface. (<b>c</b>). CaCO<sub>3</sub> salt deposition on the FAS-CNIM surface. (<b>d</b>). CaCO<sub>3</sub> and CaSO<sub>4</sub> deposition on the PTFE membrane surface. (<b>e</b>). CaCO<sub>3</sub> and CaSO<sub>4</sub> deposition on the CNIM surface. (<b>f</b>). CaCO<sub>3</sub> and CaSO<sub>4</sub> deposition on the FAS-CNIM surface. The temperature for this fouling experiment was 80 °C with a flow rate of 120 mL/min. (Single salt: CaCO<sub>3</sub> 2.8g/L, mixed salt: 2.8 g/L CaCO<sub>3</sub> and 6.6 g/L CaSO<sub>4</sub>.).</p>
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<p>The mechanism of salt rejection and vapor transport through the membrane.</p>
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31 pages, 21161 KiB  
Article
Ni-B-PTFE Nanocomposite Co-Deposition on the Surface of 2A12 Aluminum Alloy
by Shunqi Mei, Zekui Hu, Jinyu Yang, Jia Chen, Quan Zheng, Burial Lygdenov and Guryev Alexey
Materials 2024, 17(13), 3294; https://doi.org/10.3390/ma17133294 - 3 Jul 2024
Viewed by 1152
Abstract
The spinning cup, a crucial component of textile equipment, relies heavily on 2A12 aluminum alloy as its primary raw material. Commonly, electroplating and chemical nickel–phosphorus (Ni-P) plating are employed to improve the surface characteristics of the object. Nevertheless, due to the growing expectations [...] Read more.
The spinning cup, a crucial component of textile equipment, relies heavily on 2A12 aluminum alloy as its primary raw material. Commonly, electroplating and chemical nickel–phosphorus (Ni-P) plating are employed to improve the surface characteristics of the object. Nevertheless, due to the growing expectations for the performance of aluminum alloys, the hardness and wear resistance of Ni-P coatings are no longer sufficient to fulfill industry standards. This study primarily focuses on the synthesis of Ni-B-PTFE nanocomposite chemical plating and its effectiveness when applied to the surface of 2A12 aluminum alloy. We examine the impact of the composition of the plating solution, process parameters, and various other factors on the pace at which the coating is deposited, the hardness of the surface, and other indicators of the coating. The research findings indicate that the composite co-deposited coating achieves its optimal surface morphology when the following conditions are met: a nickel chloride concentration of 30 g/L, an ethylenediamine concentration of 70 mL, a sodium borohydride concentration of 0.6 g/L, a sodium hydroxide concentration of 90 g/L, a lead nitrate concentration of 30 mL, a pH value of 12, a temperature of 90 °C, and a PTFE concentration of 10 mL/L. The coating exhibits consistency, density, a smooth surface, and an absence of noticeable pores or fissures. The composite co-deposited coating exhibits a surface hardness of 1109 HV0.1, which significantly surpasses the substrate’s hardness of 232.38 HV0.1. The Ni-B-PTFE composite coating exhibits an average friction coefficient of around 0.12. It has a scratch width of 855.18 μm and a wear mass of 0.05 mg. This coating demonstrates superior wear resistance when compared to Ni-B coatings. The Ni-B-PTFE composite coating specimen exhibits a self-corrosion potential of −6.195 V and a corrosion current density of 7.81 × 10−7 A/cm2, which is the lowest recorded. This enhances its corrosion resistance compared to Ni-B coatings. Full article
(This article belongs to the Section Advanced Nanomaterials and Nanotechnology)
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<p>Physical image of standard electroless plating specimens.</p>
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<p>Schematic diagram of Ni-B electroless plating experimental platform.</p>
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<p>VDI 3198 indentation test principle.</p>
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<p>Schematic diagram of PTFE composite co-deposition principle.</p>
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<p>(<b>a</b>) Normal electroless nickel plating solution (<b>b</b>) Electroless nickel plating solution for decomposition.</p>
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<p>(<b>a</b>) Peeling nickel-boron plating, (<b>b</b>) Missing nickel-boron plating, (<b>c</b>) Normal nickel-boron plating.</p>
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<p>Measurement of Ni-B coating thickness.</p>
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<p>Intuitive effect graph of deposition rate.</p>
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<p>Intuitive effect graph of microhardness.</p>
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<p>Microscopic appearance of coating adhesion in some samples.</p>
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<p>(<b>a</b>) Nickel-boron plating at a magnification of 500 times, (<b>b</b>) Nickel-boron plating at a magnification of 2000 times, (<b>c</b>) Cross-section of the plating under an optical microscope.</p>
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<p>Comparison of microhardness between substrate and the optimal Ni-B coating test sample.</p>
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<p>Elemental distribution map of the Ni-B coating.</p>
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<p>The X-ray diffraction (XRD) spectrum of the most effective nickel–boron (Ni-B) coating applied to the surface of the 2A12 aluminum alloy.</p>
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<p>(<b>a</b>) nickel-boron coated sample, (<b>b</b>) nickel-boron polytetrafluoroethylene coated sample.</p>
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<p>Microstructure of the composite coating with 4 mL/L PTFE concentration.</p>
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<p>Composite coating microstructure with a 6 mL/L PTFE concentration.</p>
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<p>Composite coating microstructure with a 8 mL/L PTFE concentration.</p>
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<p>Composite coating microstructure with a 10 mL/L PTFE concentration.</p>
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<p>Composite coating microstructure with a 12 mL/L PTFE concentration.</p>
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<p>Microhardness of composite coatings with different PTFE concentrations.</p>
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<p>(<b>a</b>) Elemental scan of Ni-B coating, (<b>b</b>) Elemental scan of composite coating with PTFE emulsion concentration of 4 mL/L. (<b>c</b>) Elemental scan of composite coating with PTFE emulsion concentration of 6 mL/L, (<b>d</b>) Elemental scan of composite coating with PTFE emulsion concentration of 8 mL/L. (<b>e</b>) Elemental scan of composite coating at 10 mL/L PTFE emulsion concentration, (<b>f</b>) Elemental scan of composite coating at 12 mL/L PTFE emulsion concentration.</p>
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<p>XRD spectrum of the optimal Ni-B-PTFE coating on the surface of 2A12 aluminum alloy.</p>
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<p>Graph of friction coefficient vs. time relationship.</p>
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<p>Surface morphology of the wear track on the 2A12 aluminum alloy substrate.</p>
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<p>Surface morphology of the wear track on the optimal Ni-B coating of 2A12 aluminum alloy.</p>
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<p>Surface morphology of the wear track on the Ni-B-PTFE coating of 2A12 aluminum alloy.</p>
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<p>(<b>a</b>) 3D abrasion morphology of matrix sample, (<b>b</b>) 3D abrasion morphology of nickel-boron coated sample, (<b>c</b>) 3D abrasion morphology of nickel-boron PTFE sample.</p>
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<p>Polarization curves of different samples.</p>
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<p>(<b>a</b>) Nyquist diagram of 2A12 aluminium alloy matrix sample, (<b>b</b>) bode diagram of 2A12 aluminium alloy matrix sample.</p>
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<p>(<b>a</b>) Nyquist diagram of Ni-B coated sample, (<b>b</b>) bode diagram of Ni-B coated sample.</p>
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<p>(<b>a</b>) Nyquist diagram of Ni-B-PTFE coated sample, (<b>b</b>) bode diagram of Ni-B-PTFE coated sample.</p>
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14 pages, 3961 KiB  
Article
In Vivo Durability of Polyurethane Insulated Implantable Cardioverter Defibrillator (ICD) Leads
by Anmar Salih and Tarun Goswami
Polymers 2024, 16(12), 1722; https://doi.org/10.3390/polym16121722 - 17 Jun 2024
Viewed by 1200
Abstract
The 6935M Sprint Quattro Secure S and 6947M Sprint Quattro Secure are high voltage leads designed to administer a maximum of 40 joules of energy for terminating ventricular tachycardia or ventricular fibrillation. Both leads utilize silicone insulation and a polyurethane outer coating. The [...] Read more.
The 6935M Sprint Quattro Secure S and 6947M Sprint Quattro Secure are high voltage leads designed to administer a maximum of 40 joules of energy for terminating ventricular tachycardia or ventricular fibrillation. Both leads utilize silicone insulation and a polyurethane outer coating. The inner coil is shielded with polytetrafluoroethylene (PTFE) tubing, while other conductors are enveloped in ethylene tetrafluoroethylene (ETFE), contributing to the structural integrity and functionality of these leads. Polyurethane is a preferred material for the outer insulation of cardiac leads due to its flexibility and biocompatibility, while silicone rubber ensures chemical stability within the body, minimizing inflammatory or rejection responses. Thirteen implantable cardioverter defibrillator (ICD) leads were obtained from the Wright State University Anatomical Gift Program. The as-received devices exhibited varied in vivo implantation durations ranging from less than a month to 89 months, with an average in vivo duration of 41 ± 27 months. Tests were conducted using the Test Resources Q series system, ensuring compliance with ASTM Standard D 1708-02a and ASTM Standard D 412-06a. During testing, a load was applied to the intact lead, with careful inspection for surface defects before each test. Results of load to failure, percentage elongation, percentage elongation at 5 N, ultimate tensile strength, and modulus of elasticity were calculated. The findings revealed no significant differences in these parameters across all in vivo exposure durations. The residual properties of these ICD leads demonstrated remarkable stability and performance over a wide range of in vivo exposure durations, with no statistically significant degradation or performance changes observed. Full article
(This article belongs to the Section Polymer Processing and Engineering)
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<p>ICD leads used in the investigation: (<b>A</b>) 6947M Sprint Quattro Secure features dual coils and (<b>B</b>) 6935M Sprint Quattro Secure S with a single coil.</p>
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<p>ICD lead design, featuring silicone insulation and a polyurethane outer coating. Each lumen is designated for high voltage and pace–sense conductors. The inner coil is protected by polytetrafluoroethylene (PTFE) tubing, while other conductors are encased in ethylene tetrafluoroethylene (ETFE), enhancing the structural integrity and functionality of the leads [<a href="#B9-polymers-16-01722" class="html-bibr">9</a>].</p>
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<p>(<b>A</b>) Cross section of the lead, (<b>B</b>) length of lead and in the grip with 8 mm (<b>C</b>) during the test procedure.</p>
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<p>(<b>A</b>) shows the mean maximum load to failure vs. number of in vivo months of exposure, (<b>B</b>) shows the mean maximum load to failure vs. age, and (<b>C</b>) shows the mean maximum load to failure vs. gender.</p>
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<p>(<b>A</b>) shows the mean maximum percentage of elongation vs. number of in vivo months of exposure, (<b>B</b>) shows the mean maximum percentage of elongation vs. age, and (<b>C</b>) shows the mean maximum percentage of elongation vs. gender.</p>
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<p>(<b>A</b>) shows the mean percentage elongation at 5 N vs. number of in vivo months of exposure, (<b>B</b>) shows the mean percentage elongation at 5 N vs. age, and (<b>C</b>) shows the mean percentage elongation at 5 N vs. gender.</p>
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<p>(<b>A</b>) shows the mean ultimate tensile strength vs. number of in vivo months of exposure, (<b>B</b>) shows the mean ultimate tensile strength vs. age, and (<b>C</b>) shows the mean ultimate tensile strength vs. gender.</p>
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<p>(<b>A</b>) shows the mean modulus of elasticity vs. number of in vivo months of exposure, (<b>B</b>) shows the mean modulus of elasticity vs. age, and (<b>C</b>) shows the mean modulus of elasticity vs. gender.</p>
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<p>Correlation between load to failure, maximum elongation, percentage elongation at 5 N force, ultimate tensile strength, and modulus of elasticity.</p>
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<p>Probability of failure to each residual property with respect to (<b>A</b>) load to failure, (<b>B</b>) percentage elongation to failure, (<b>C</b>) percentage elongation at 5 N force, (<b>D</b>) ultimate tensile strength, and (<b>E</b>) modulus of elasticity.</p>
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17 pages, 13344 KiB  
Article
Effect of Polytetrafluoroethylene Coating on Corrosion Wear Properties of AZ31 Magnesium Alloy by Electrophoretic Deposition
by Jilun Zhang, Chaoyi Chen, Junqi Li and Li Chen
Coatings 2024, 14(6), 664; https://doi.org/10.3390/coatings14060664 - 24 May 2024
Cited by 1 | Viewed by 780
Abstract
In this study, we aim to enhance the corrosion and wear resistance of AZ31 magnesium alloy using electrophoretic deposition (EPD) technology to apply a hydrophobic polytetrafluoroethylene (PTFE) coating. Polyethyleneimine (PEI) serves as a charged dispersant, facilitating uniform deposition of PTFE particles on the [...] Read more.
In this study, we aim to enhance the corrosion and wear resistance of AZ31 magnesium alloy using electrophoretic deposition (EPD) technology to apply a hydrophobic polytetrafluoroethylene (PTFE) coating. Polyethyleneimine (PEI) serves as a charged dispersant, facilitating uniform deposition of PTFE particles on the alloy surface. Results demonstrate a significant reduction in corrosion current density (from 67.5 μA/cm2 to 5.2 μA/cm2) and improved wear resistance (wear volume decreased from 0.24167 mm3 to 0.00167 mm3) in a 3.5 wt% NaCl solution compared to uncoated alloy. Moreover, the friction coefficient of the coated sample decreases. These findings underscore the potential of nano-PTFE coatings prepared via EPD in enhancing AZ31 magnesium alloy’s corrosion and wear resistance, providing a foundation for future protective coating design and optimization. Full article
(This article belongs to the Special Issue Thin-Film Synthesis, Characterization and Properties)
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<p>(<b>a</b>) SEM, (<b>b</b>) EDS, and (<b>c</b>) the particle size distribution of the PTFE.</p>
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<p>The schematic of the homemade reciprocating friction tester.</p>
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<p>Trend of the impact of additive on the zeta potential.</p>
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<p>Cross-sectional micrographs of PTFE coatings deposited for (<b>a</b>) 5 min, (<b>b</b>) 10 min, and (<b>c</b>) 15 min.</p>
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<p>The cross-sectional micrographs: (<b>a</b>) 200× and (<b>d</b>) 500× magnification of PTFE coating (deposition 5 min), (<b>b</b>) 200× and (<b>e</b>) 500× magnification of PTFE coating (deposition 10 min), (<b>c</b>) 200× and (<b>f</b>) 500× magnification of PTFE coating (deposition 15 min).</p>
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<p>(<b>a</b>) XRD patterns of PTFE coatings and AZ31 Mg alloy, (<b>b</b>) FTIR data for PTFE coating.</p>
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<p>Plot of contact angles of water. Here, the black sign above the bars represents the water contact angle.</p>
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<p>Potential dynamic polarization curves in the 3.5 wt% NaCl solution of various time-deposited coatings.</p>
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<p>Electrochemical impedance spectra of unprotected and protected AZ31 Mg alloy, (<b>a</b>) Nyquist and (<b>b</b>) Impedance Modulus and Bode graphs, (<b>c</b>,<b>d</b>) comparable schematics for circuits. Here, <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>C</mi> <mi>P</mi> <mi>E</mi> </mrow> <mrow> <mi>P</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>R</mi> </mrow> <mrow> <mi>P</mi> </mrow> </msub> </mrow> </semantics></math> are the double-layer capacitance of electrolyte and substrate, and charge transfer resistance, respectively.</p>
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<p>The surface micrographs of PTFE-coated Mg AZ31 and EDS of the coating deposited 5 min. (<b>a</b>) deposited for 5 mim; (<b>b</b>) deposited for 10 min; (<b>c</b>) EDS for 5 min (<b>d</b>) deposited for 15 min.</p>
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<p>Curves of the time-friction coefficient for raw samples and different coating qualities under 1 N loads.</p>
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<p>Samples of raw and varied coating quality wear loss under 1 N load. 1# raw sample, 2# deposited 5 min, 3# deposited 10 min, 4# deposited 15 min.</p>
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<p>Under 1 N stress, the 3D morphology and profile of (<b>a</b>) the bare sample, (<b>b</b>) the sample deposited for 5 min, (<b>c</b>) the sample deposited for 10 min, and (<b>d</b>) the sample deposited for 15 min, as well as (<b>e</b>) the profiles of the raw sample and the samples deposited for 5 min, 10 min, and 15 min.</p>
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<p>Wear morphology of raw and PTFE coating under 1 N loads of (<b>a</b>) raw sample, (<b>b</b>) 5 min, (<b>c</b>) 10 min.</p>
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<p>Schematic diagram of abrasion mechanism of AZ31 magnesium alloy after electrophoretic deposition of PTFE coating treatment.</p>
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19 pages, 4454 KiB  
Article
Robust CA-GO-TiO2/PTFE Photocatalytic Membranes for the Degradation of the Azithromycin Formulation from Wastewaters
by Veronica Satulu, Andreea Madalina Pandele, Giovanina-Iuliana Ionica, Liliana Bobirică, Anca Florina Bonciu, Alexandra Scarlatescu, Constantin Bobirică, Cristina Orbeci, Stefan Ioan Voicu, Bogdana Mitu and Gheorghe Dinescu
Polymers 2024, 16(10), 1368; https://doi.org/10.3390/polym16101368 - 10 May 2024
Cited by 3 | Viewed by 1390
Abstract
We have developed an innovative thin-film nanocomposite membrane that contains cellulose acetate (CA) with small amounts of TiO2-decorated graphene oxide (GO) (ranging from 0.5 wt.% to 2 wt.%) sandwiched between two polytetrafluoroethylene (PTFE)-like thin films. The PTFE-like films succeeded in maintaining [...] Read more.
We have developed an innovative thin-film nanocomposite membrane that contains cellulose acetate (CA) with small amounts of TiO2-decorated graphene oxide (GO) (ranging from 0.5 wt.% to 2 wt.%) sandwiched between two polytetrafluoroethylene (PTFE)-like thin films. The PTFE-like films succeeded in maintaining the bulk porosity of the support while increasing the thermal and chemical robustness of the membrane and boosting the catalytic activity of TiO2 nanoparticles. The membranes exhibited a specific chemical composition and bonding, with predominant carbon–oxygen bonds from CA and GO in the bulk, and carbon–fluorine bonds on their PTFE-like coated sides. We have also tested the membranes’ photocatalytic activities on azithromycin-containing wastewaters, demonstrating excellent efficiency with more than 80% degradation for 2 wt.% TiO2-decorated GO in the CA-GO-TiO2/PTFE-like membranes. The degradation of the azithromycin formulation occurs in two steps, with reaction rates being correlated to the amount of GO-TiO2 in the membranes. Full article
(This article belongs to the Special Issue Advances in Cellulose-Based Polymers and Composites)
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<p>Illustration of the steps involved in the preparation of the CA-GO-TiO<sub>2</sub> membranes.</p>
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<p>Schematic illustration of the deposition process of PTFE-like thin films via magnetron sputtering for the creation of composite membranes with superior chemical robustness; the different colored ovals in the diagram representing the film describe the incorporation of different species and radicals, suchas C-C, CF, C-CF, CF<sub>2</sub>, and CF<sub>3</sub>, in the deposited material.</p>
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<p>Schematic illustration of the reactor for photocatalytic oxidation with continuous recirculation.</p>
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<p>SEM images (magnification 50,000×) of the initial CA-GO-TiO<sub>2</sub> membranes’ surfaces with various TiO<sub>2</sub>-decorated GO concentrations and of TFC composite membranes coated with a 200 nm PTFE-like layer. The yellow boxes identify the processed regions of the SEM images presented in the corner of each image in order to better evidence the sample porosity before and after the PTFE-like coating.</p>
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<p>Cross-sections through 3D reconstruction of the microtomographies of the initial CA-GO0.5%-TiO<sub>2</sub> and coated CA-GO0.5%-TiO<sub>2</sub>/PTFE; lateral dimension in the reconstructed image is 250 μm on both sides.</p>
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<p>Comparative XPS spectra for the initial and PTFE-like coated CA-GO-TiO<sub>2</sub> membranes: (<b>a</b>) survey spectra and elemental concentration evidencing the modification of surface chemistry; (<b>b</b>) binding energy region and bonding identification of C1s; (<b>c</b>) deconvolution of the initial CA-GO2%-TiO<sub>2</sub> membrane with the labeling of the specific peaks; (<b>d</b>) deconvolution of the CA-GO2%-TiO<sub>2</sub>/PTFE with the peak labels that evidence the formation of a PTFE-like coating on the membrane’s surface.</p>
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<p>Dependence of the carbon-based bonds as a function of the GO concentration in the CA-GO-TiO<sub>2</sub> membranes.</p>
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<p>FTIR spectra of the CA-GO 2.0%-TiO<sub>2</sub> composite membrane (green line) and CA-GO 2.0%-TiO<sub>2</sub>/PTFE thin-film composite membrane (red line).</p>
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<p>Thermograms of CA-GO1%-TiO<sub>2</sub>/PTFE TFC membranes: TGA (<b>a</b>) and DTC (<b>b</b>) curves for CA, CA-GO1%-TiO<sub>2</sub>, and CA-GO1%-TiO<sub>2</sub>/PTFE membranes; (<b>c</b>) identification of the starting point (T<sub>onset</sub>), the point of the maximum degradation rate (T<sub>inflection</sub>), and the ending point (T<sub>endset</sub>) of the degradation process.</p>
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<p>Kinetics of the photocatalytic degradation of the organic content of the Azitrox formulation using the as-obtained CA-GO-TiO<sub>2</sub>/PTFE photocatalytic membranes: (<b>a</b>) COD values against time; (<b>b</b>) COD values against time and ln(C<sub>0</sub>/C) against time. The graphs illustrate a pseudo-first-order photocatalytic reaction taking place in 2 stages for the CA-GO2%-TiO<sub>2</sub>/PTFE membrane.</p>
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<p>Efficiency of the Azitrox formulation’s degradation via the photocatalytic CA-GO-TiO<sub>2</sub>/PTFE membrane.</p>
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15 pages, 4622 KiB  
Article
Dual-Function Hybrid Coatings Based on Polytetrafluoroethylene and Cu2O for Anti-Biocorrosion and Anti-Wear Applications
by Guohui Li, Huan Li, Yongkun Xu, Ren He, Ga Zhang and Zongzhu Liu
Coatings 2024, 14(5), 592; https://doi.org/10.3390/coatings14050592 - 9 May 2024
Viewed by 1190
Abstract
Corrosion and wear issues of motion components exposed to water-based corrosion mediums, e.g., naval vessels and oil extraction equipment, pose challenges for the lifespan and reliability of the motion systems. In this work, epoxy-based coatings modified with polytetrafluoroethylene (PTFE) and cuprous oxide (Cu [...] Read more.
Corrosion and wear issues of motion components exposed to water-based corrosion mediums, e.g., naval vessels and oil extraction equipment, pose challenges for the lifespan and reliability of the motion systems. In this work, epoxy-based coatings modified with polytetrafluoroethylene (PTFE) and cuprous oxide (Cu2O) nanoparticles were prepared. The anti-corrosion performance of the coatings was comparatively investigated by electrical impedance spectroscopy and Tafel tests in sterile and sulphate-reducing bacteria (SRB) mediums. Moreover, the tribological behaviors of the coatings were examined under water lubrication conditions. Our results demonstrate that the epoxy coatings lower significantly the corrosion current density icorr and the charge transfer resistance of the electrical double layer Rct of the carbon steel substrate. Interestingly, the hybrid coatings filled with both PTFE and Cu2O exhibit excellent anti-corrosion and anti-wear performance. After being immersed in the SRB medium for 18 days, the icorr of the pure EP coating and hybrid coatings are 1.10 × 10−7 Amp/cm2 and 0.3 × 10−7 Amp/cm2, and the Rct values are 1.04 × 103 Ω·cm2 and 3.87 × 103 Ω·cm2, respectively. A solid tribofilm forms on the stainless steel counterface sliding against the hybrid coating, which is surmised to be essential for the low friction coefficients and wear. The present work paves a route for formulating the dual-function coatings of anti-biocorrosion and anti-wear. Full article
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<p>(<b>a</b>) SEM graph of PTFE powder and (<b>b</b>) TEM graph of Cu<sub>2</sub>O nanoparticles.</p>
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<p>Nyquist plots of Q20 steel after immersion in sterile (<b>a</b>) and SRB mediums (<b>b</b>); Nyquist plots of coatings after immersion in sterile (<b>c</b>) and SRB mediums (<b>d</b>); equivalent circuit models for Q20 steel (<b>e1</b>) and coatings (<b>e2</b>).</p>
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<p>Potentiodynamic polarization curves of the Q20 steel (<b>a</b>,<b>b</b>) and the coatings (<b>c</b>,<b>d</b>) after being immersed in sterile (<b>a</b>,<b>c</b>) and SRB mediums (<b>b</b>,<b>d</b>) for 18 days.</p>
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<p>SEM graphs and EDS elemental maps of carbon steel surfaces after being immersed in the sterile medium (<b>a</b>) and the SRB medium (<b>b</b>,<b>c</b>) for 18 days.</p>
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<p>XPS spectra of Q20 steel surfaces after being immersed in the sterile medium (<b>a</b>,<b>a1</b>,<b>a2</b>) and the SRB medium (<b>b</b>,<b>b1</b>,<b>b2</b>) for 18 days.</p>
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<p>SEM images of EP in (<b>a</b>) sterile and (<b>b</b>) SRB medium for 18 days; SEM images of EP/1.5Cu<sub>2</sub>O/15PTFE in the (<b>c</b>) sterile and (<b>d</b>) SRB medium for 18 days.</p>
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<p>(<b>a</b>) Evolutions of friction coefficients of EP, EP/1.5Cu<sub>2</sub>O, EP/15PTFE and EP/1.5Cu<sub>2</sub>O/15PTFE; (<b>b</b>) mean friction coefficients and specific wear rates of the coatings investigated.</p>
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<p>SEM graphs of worn surfaces of EP (<b>a</b>), EP/1.5Cu<sub>2</sub>O (<b>b</b>), EP/15PTFE (<b>c</b>) and EP/1.5Cu<sub>2</sub>O/15PTFE (<b>d</b>) sliding against the steel surface in water lubrication. Arrows indicate the sliding direction.</p>
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<p>XPS spectra of the steel surface sliding against EP/1.5Cu<sub>2</sub>O/15PTFE.</p>
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