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Polymers, Volume 16, Issue 12 (June-2 2024) – 143 articles

Cover Story (view full-size image): The potential of waste plastic bags as a sustainable modifier for bitumen was investigated. These bags, primarily composed of Low-Density Polyethylene (LDPE) and Linear Low-Density Polyethylene (LLDPE) with a small percentage of impurities, were found to significantly enhance the rutting resistance of bitumen, raising its performance by one grade. This improvement positions waste plastic bags as an effective substitute for virgin LLDPE in bitumen applications. While the modified bitumen showed slightly reduced thermal and aging resistance due to the impurities, the overall results highlight the viability of waste plastic bags in promoting sustainable construction materials. View this paper
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20 pages, 3584 KiB  
Article
Study on Adsorption Characteristics and Water Retention Properties of Attapulgite–Sodium Polyacrylate and Polyacrylamide to Trace Metal Cadmium Ion
by Ziming Cai, Feng Zhan, Yingnan Wang, Meiling Wu, Lingjian Kong, An Wang and Zhanbin Huang
Polymers 2024, 16(12), 1756; https://doi.org/10.3390/polym16121756 - 20 Jun 2024
Viewed by 1098
Abstract
The adsorption mechanism of superabsorbent polymer (SAP) can provide theoretical guidance for their practical applications in different environments. However, there has been limited research on the mechanism of attapulgite–sodium polyacrylate. This research aimed to compare the Cd(II) adsorption characteristics and water retention properties [...] Read more.
The adsorption mechanism of superabsorbent polymer (SAP) can provide theoretical guidance for their practical applications in different environments. However, there has been limited research on the mechanism of attapulgite–sodium polyacrylate. This research aimed to compare the Cd(II) adsorption characteristics and water retention properties of organic–inorganic composite SAP (attapulgite–sodium polyacrylate, OSAP) and organic SAP (polyacrylamide, JSAP). Batch experiments were used to investigate the kinetics of Cd(II) adsorption, as well as the thermodynamic properties and factors influencing these properties. The results show that the Cd(II) adsorption capacity was directly proportional to the pH value. The maximum adsorption capacities of OSAP and JSAP were of 770 and 345 mg·g−1. The Cd(II) adsorption for OSAP and JSAP conformed to the Langmuir and the quasi-second-order kinetic model. This indicates that chemical adsorption is the primary mechanism. The adsorption process was endothermic (ΔH0 > 0) and spontaneous (ΔG0 < 0). The water adsorption ratios of OSAP and SAP were 474.8 and 152.6 in pure water. The ratio decreases with the increase in Cd(II) concentration. OSAP and JSAP retained 67.23% and 38.37% of the initial water adsorption after six iterations of water adsorption. Hence, OSAP is more suitable than JSAP for agricultural and environmental ecological restoration in arid and semi-arid regions. Full article
(This article belongs to the Section Polymer Analysis and Characterization)
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<p>Superabsorbent polymers. (<b>a</b>) OSAP; (<b>b</b>) JSAP.</p>
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<p>Cd(II) adsorption capacities by SAP in different dosages.</p>
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<p>Cd(II) adsorption capacities by SAP in different initial Cd(II) concentrations. (<b>a</b>) Langmuir and Freundlich model; (<b>b</b>) Temkin model.</p>
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<p>Cd(II) adsorption capacities by SAP at different pH levels.</p>
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<p>Effect of different temperatures 15° (<b>a</b>), 25° (<b>b</b>), 35° (<b>c</b>) on the adsorption of Cd(II).</p>
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<p>Cd(II) desorption capacity and desorption rate by (<b>a</b>) OSAP and (<b>b</b>) JSAP in different pH levels.</p>
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<p>Thermodynamic parameter fitting graph.</p>
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<p>Cd(II) adsorption capacities by SAP in different contact times.</p>
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<p>(<b>a</b>) The XPS survey spectra, (<b>b</b>) C 1s XPS spectra, and (<b>c</b>) O 1s XPS spectra of OSAP and JSAP before and after Cd(II) adsorption.</p>
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<p>(<b>a</b>) The XPS survey spectra, (<b>b</b>) C 1s XPS spectra, and (<b>c</b>) O 1s XPS spectra of OSAP and JSAP before and after Cd(II) adsorption.</p>
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<p>SEM micrographs. (<b>a</b>) OSAP; (<b>b</b>) OSAP-Cd; (<b>c</b>) JSAP; (<b>d</b>) JSAP-Cd.</p>
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<p>FTIR spectra of OSAP, JSAP, OSAP-Cd, and JSAP-Cd.</p>
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<p>Chemical structure. (<b>a</b>) Attapulgite; (<b>b</b>) OSAP [<a href="#B35-polymers-16-01756" class="html-bibr">35</a>]; (<b>c</b>) Polyacrylamide; (<b>d</b>) Broken carbon–nitrogen bond; (<b>e</b>) Broken amide bond; (<b>f</b>) Broken carbon–carbon bond.</p>
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<p>Mechanistic analysis.</p>
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<p>(<b>a</b>) Water adsorption ratio at different Cd concentrations. Repeated water adsorption of (<b>b</b>) OSAP and (<b>c</b>) JSAP. Water-retaining property of (<b>d</b>) OSAP and (<b>e</b>) JSAP.</p>
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<p>(<b>a</b>) Water adsorption ratio at different Cd concentrations. Repeated water adsorption of (<b>b</b>) OSAP and (<b>c</b>) JSAP. Water-retaining property of (<b>d</b>) OSAP and (<b>e</b>) JSAP.</p>
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10 pages, 2275 KiB  
Article
Molecular Dynamics Simulation of Silicone Oil Polymerization from Combined QM/MM Modeling
by Pascal Puhlmann and Dirk Zahn
Polymers 2024, 16(12), 1755; https://doi.org/10.3390/polym16121755 - 20 Jun 2024
Cited by 1 | Viewed by 1187
Abstract
We outline a molecular simulation protocol for elucidating the formation of silicone oil from trimethlyl- and dimethlysilanediole precursor mixtures. While the fundamental condensation reactions are effectively described by quantum mechanical calculations, this is combined with molecular mechanics models in order to assess the [...] Read more.
We outline a molecular simulation protocol for elucidating the formation of silicone oil from trimethlyl- and dimethlysilanediole precursor mixtures. While the fundamental condensation reactions are effectively described by quantum mechanical calculations, this is combined with molecular mechanics models in order to assess the extended relaxation processes. Within a small series of different precursor mixtures used as starting points, we demonstrate the evolution of the curing degree and heat formation in the course of polymer chain growth. Despite the increasing complexity of the amorphous agglomerate of polymer chains, our approach shows an appealing performance for tackling both elastic and viscous relaxation. Indeed, the finally obtained polymer systems feature 99% curing and thus offer realistic insights into the growth mechanisms of coexisting/competing polymer strands. Full article
(This article belongs to the Special Issue Molecular Dynamics Simulation of Polymeric Materials)
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<p>Polymerization of PDMS by condensation reactions. In our simulation protocol, the gas phase reaction for k = m = 1 (and imposing vaporization of the formed water molecule) is used as the QM subsystem, whereas all other degrees of freedom are treated from MM calculations.</p>
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<p>Comparison of the structure of hexamethyldisilane as obtained from dimerization of TMS. The atomic positions resulting from the MM model are shown as solid spheres (Si: yellow; O: red; C: gray; H: white), whereas the QM structure is indicated by a transparent ball and stick representation.</p>
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<p>Interplay of curing degree and relaxation times needed as observed for a typical polymerization run. Left: evolution of the acceptance probability of the individual polymerization steps as a function of η. Right: curing degree as a function of the cumulative sum of reaction attempts needed. For comparison, the dashed curves shown in green indicate an idealized scenario in which all reaction attempts are successful. The solid curves shown in blue, black, and red refer to averages taken from three independent runs each performed at 250, 300, and 350 K, respectively, whereas the root-mean-square deviations are indicated by transparent color representations.</p>
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<p>Curing of PDMS at 300 K and 1 atm using 3D periodic simulation cells. Starting from 500 DMSD precursor species, curing up to η = 99% is achieved, leading to a density increase from 0.91 g/cm<sup>3</sup> to 1.04 g/cm<sup>3</sup>, respectively. Only Si atoms are shown. In the final system, a siloxane chain of 54 DMSD building blocks is highlighted in blue. To illustrate the formation process via reactions of monomers and oligomers, the same coloring is applied to earlier stages of polymerization.</p>
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<p>Distribution of PDMS chain length as functions of (<b>a</b>) curing degree, (<b>b</b>) process temperature, and (<b>c</b>) precursor composition. The mean chain length (ν) is averaged from three independent polymerization runs. From the root-mean-square deviations we assess the polydispersity index (PDI = M<sub>w</sub>/M<sub>n</sub>) as PDI = 1.73/1.49/1.59 and PDI = 1.49/1.60/1.91, as functions of temperature (T = 250/300/350 K and 100% DMSD precursors) and composition (0/10/20% TMS and T = 300 K), respectively.</p>
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<p>Heat of individual reaction steps as observed during the curing of PDMS. Data are shown for various DMSD/TMS precursor mixtures, all cured at 300 K and 1 atm, respectively. The curves shown in black refer to averages taken from three independent runs, whereas the root-mean-square deviations are indicated in gray. Left to right: profiles sampled for 0/10/20% TMS content, respectively, showing rough constant reaction heat (&lt;ΔH&gt;<sub>0&lt;η&lt;70%</sub> = 0.26/0.25/0.26 eV, as indicated by the dashed lines) up to η &lt; 70%. Upon curing by 99%, the reaction heat is gradually reduced by about 0.1 eV because of the mechanical strain within the (amorphous) agglomerates of PDMS chains. The overall heat of formation is sampled as &lt;ΔH&gt;<sub>0&lt;η&lt;99%</sub> = 0.24/0.24/0.24 eV per monomeric unit for the silicone oils prepared from DMSD/TMS precursor mixtures of 0/10/20% TMS content, respectively.</p>
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<p>Characterization of the finally obtained silicone oil models from curing the precursor systems of 0/10/20% TMS content at 300 K and 1 atm. Left: radial distribution functions of the Si-O distances. Right: mean-squared-deviation profiles as function of time as used for assessing the diffusion constants. For the latter, linear fits are applied to the last 7 ns, as indicated by the dashed lines.</p>
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19 pages, 4178 KiB  
Article
Cross-Scale Industrial Manufacturing of Multifunctional Glass Fiber/Epoxy Composite Tubes via a Purposely Modified Filament Winding Production Line
by George Karalis, Lampros Koutsotolis, Angelos Voudouris Itksaras, Thomai Tiriakidi, Nikolaos Tiriakidis, Kosmas Tiriakidis and Alkiviadis S. Paipetis
Polymers 2024, 16(12), 1754; https://doi.org/10.3390/polym16121754 - 20 Jun 2024
Viewed by 1132
Abstract
In the present research work is demonstrated a cross-scale manufacturing approach for the production of multifunctional glass fiber reinforced polymer (GFRP) composite tubes with a purposely redesigned filament winding process. Up until now, limited studies have been reported towards the multiscale reinforcement direction [...] Read more.
In the present research work is demonstrated a cross-scale manufacturing approach for the production of multifunctional glass fiber reinforced polymer (GFRP) composite tubes with a purposely redesigned filament winding process. Up until now, limited studies have been reported towards the multiscale reinforcement direction of continuous fibers for the manufacturing of hierarchical composites at the industrial level. This study involved the development of two different multi-walled carbon nanotube (MWCNT) aqueous-based inks, which were employed for the modification of commercial glass fiber (GF) reinforcing tows via a bath coating unit in a pilot production line. The obtained multifunctional GFRP tubes presented a variety of characteristics in relation to their final mechanical, hydrothermal aging, electrical, thermal and thermoelectric properties. Results revealed that the two individual systems exhibited pronounced differences both in crushing behavior and durability performance. Interestingly, for lateral compression the MWCNT coatings comprising a polymeric dispersant minorly affected the mechanical response of the produced tubes. The crashworthiness indicators of the multifunctional tubes displayed a slight 5% variation to the respective reference values, combined with a more ductile behavior. Moreover, regarding the bulk electrical and thermal conductivity values, as well as the Seebeck coefficient factor, the corresponding tubes displayed a variance of 233% and 19% and an opposite semi-conducting sign denoting a p- and n-type character, respectively. Full article
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<p>(<b>a</b>) Schematic representation of the purposely modified filament winding production line and various snapshots of the redesigned filament winding steps for the cross-scale manufacturing of multifunctional GFRP tubes: (<b>b</b>) MWCNT-based ink bath for GF tows coating process after the electronic tensioner, (<b>c</b>) high-temperature drying system with IR lamps for the rapid aqueous solvent evaporation, (<b>d</b>) resin bath impregnation of the coated GF-MWCNT tows and guidance to the ceramic ills for protection and further alignment, (<b>e</b>) winding process and (<b>f</b>) final coated GF-MWCNT tows and multifunctional GFRP tubes.</p>
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<p>FESEM captures at different magnifications for the (<b>a</b>) bare GF tow, (<b>b</b>) coated GF-MWCNT:SDBS tow and (<b>c</b>) coated GF-MWCNT:PVP tow.</p>
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<p>(<b>a</b>) Raman spectra and (<b>b</b>) TGA measurements for the coated GF-MWCNT:SDBS and coated GF-MWCNT:PVP tows.</p>
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<p>Representative load-displacement curves for (<b>a</b>) lateral and (<b>b</b>) axial crushing.</p>
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<p>Crushing history under lateral compression.</p>
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<p>Crushing history under axial compression.</p>
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<p>3D and cross-sectional images of the horizontal (XY) and the vertical (XZ) plane. Tubes are shown in the undamaged state, after the first failure under lateral compression, after test and at the end of the test under axial compression.</p>
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<p>Moisture absorption as a function of the square root of the exposure time.</p>
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<p>Measuring configurations and comparison graphs of the (<b>a</b>) electric and (<b>b</b>) thermoelectric response for in-plane and through-thickness measurements resulting from the two different systems of multifunctional GFRP tubes.</p>
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12 pages, 7233 KiB  
Article
Additive Manufacturing of Head Surrogates for Evaluation of Protection in Sports
by Ramiro Mantecón, Borja Valverde-Marcos, Ignacio Rubio, George Youssef, José Antonio Loya, José Díaz-Álvarez and María Henar Miguélez
Polymers 2024, 16(12), 1753; https://doi.org/10.3390/polym16121753 - 20 Jun 2024
Viewed by 1193
Abstract
Head impacts are a major concern in contact sports and sports with high-speed mobility due to the prevalence of head trauma events and their dire consequences. Surrogates of human heads are required in laboratory testing to safely explore the efficacy of impact-mitigating mechanisms. [...] Read more.
Head impacts are a major concern in contact sports and sports with high-speed mobility due to the prevalence of head trauma events and their dire consequences. Surrogates of human heads are required in laboratory testing to safely explore the efficacy of impact-mitigating mechanisms. This work proposes using polymer additive manufacturing technologies to obtain a substitute for the human skull to be filled with a silicone-based brain surrogate. This assembly was instrumentalized with an Inertial Measurement Unit. Its performance was compared to a standard Hybrid III head form in validation tests using commercial headgear. The tests involved impact velocities in a range centered around 5 m/s. The results show a reasonable homology between the head substitutes, with a disparity in the impact response within 20% between the proposed surrogate and the standard head form. The head surrogate herein developed can be easily adapted to other morphologies and will significantly decrease the cost of the laboratory testing of head protection equipment, all while ensuring the safety of the testing process. Full article
(This article belongs to the Special Issue Polymers Additive Manufacturing in Sports and Protective Equipment)
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<p>(<b>A</b>) Reference CT scan. (<b>B</b>) Segmented CAD model with only the skull of the cranial vault. (<b>C</b>) Layout of half-skull for 3D printing. (<b>D</b>) Geometry and attributes of the trilayer structure.</p>
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<p>Assembly of demonstrators with cycling helmets of (<b>A</b>) Hybrid III and (<b>B</b>) surrogate in the drop tower.</p>
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<p>Sensorization of the head forms and location of the accelerometers in (<b>A</b>) the 3D-printed head surrogate and (<b>B</b>) the Hybrid III.</p>
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<p>Calibration curves for the Hybrid III head form (blue) and the 3D-printed head surrogate (red).</p>
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<p>Acceleration–time histories as a function of drop height and velocities using cyclist helmet–Hybrid III testing construct. Shaded region is the time interval that maximizes the value of the HIC.</p>
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<p>Acceleration–time curves were measured by dropping a 3D-printed, silicone-filled head surrogate fitted with a cyclist helmet at different velocities. Shaded region is the time interval that maximizes the value of the HIC.</p>
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<p>Impact response of the two head forms represented by peak linear acceleration as a function of impact velocity. Datapoints are highlighted in circles.</p>
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21 pages, 1474 KiB  
Article
A Multi-Objective Optimization of Neural Networks for Predicting the Physical Properties of Textile Polymer Composite Materials
by Ivan Malashin, Vadim Tynchenko, Andrei Gantimurov, Vladimir Nelyub and Aleksei Borodulin
Polymers 2024, 16(12), 1752; https://doi.org/10.3390/polym16121752 - 20 Jun 2024
Cited by 2 | Viewed by 1346
Abstract
This paper explores the application of multi-objective optimization techniques, including MOPSO, NSGA II, and SPEA2, to optimize the hyperparameters of artificial neural networks (ANNs) and support vector machines (SVMs) for predicting the physical properties of textile polymer composite materials (TPCMs). The optimization process [...] Read more.
This paper explores the application of multi-objective optimization techniques, including MOPSO, NSGA II, and SPEA2, to optimize the hyperparameters of artificial neural networks (ANNs) and support vector machines (SVMs) for predicting the physical properties of textile polymer composite materials (TPCMs). The optimization process utilizes data on the physical characteristics of the constituent fibers and fabrics used to manufacture these composites. By employing optimization algorithms, we aim to enhance the predictive accuracy of the ANN and SVM models, thereby facilitating the design and development of high-performance textile polymer composites. The effectiveness of the proposed approach is demonstrated through comparative analyses and validation experiments, highlighting its potential for optimizing complex material systems. Full article
(This article belongs to the Special Issue Scientific Machine Learning for Polymeric Materials)
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<p>Physical properties of textile PCMs such as the tensile, compressive, and bending strengths and the modulus of elasticity in tension along the warp and weft directions, respectively, for the considered specimens.</p>
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<p>Distribution of the interlaminar shear modulus, coefficient of linear thermal expansion (CTE) along the warp direction, and density for the considered specimens.</p>
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<p>Histograms depicting the distribution of the physical characteristics for TPCMs grouped by type: basalt plastic, fiberglass, carbon plastic, and aramid plastic. Each subplot illustrates the distribution of the following characteristics along the main and warp directions: tensile strength, compression strength, bending strength, Young’s modulus, and ultimate elongation.</p>
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<p>Histograms of physical attributes for TPCMs grouped by type: basalt plastic, fiberglass, carbon plastic, and aramid plastic for the distributions of the interlaminar shear modulus, CTE, and density.</p>
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<p>Correlation matrix of physical properties of TPMCs (highlighted in green) and fabric properties (highlighted in red), from which the samples are derived.</p>
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<p>Illustration of a hypothetical neural network architecture designed to predict the physical characteristics of TPCMs: blue dots as inputs, red dots as outputs.</p>
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<p>Evolution of loss curves and optimization parameter space for hyperparameter tuning in the ANN and SVM using the MOPSO (<b>a</b>–<b>d</b>), SPEA2 (<b>e</b>–<b>h</b>), and NGSA-II (<b>i</b>–<b>l</b>) optimization methods.</p>
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<p>Whisker charts for selected types of TPCMs depending on physical property: (<b>a</b>) Tensile strength along the base, (<b>b</b>) Tensile strength along the warp, (<b>c</b>) Compression strength along the base, (<b>d</b>) Compression strength along the warp, (<b>e</b>) Bending strength along the base, (<b>f</b>) Bending strength along the warp with predictions made by the best architectures of the ANN (digits in yellow) and SVM (digits in cyan), architectures optimized using the MOPSO and NSGA-II algorithms, respectively.</p>
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<p>Whisker charts for selected types of TPCMs charts for selected types of TPCMs depending on physical property: (<b>a</b>) Tensile strength along the base depending on physical property: (<b>a</b>) Young’s modulus in tension along the base, (<b>b</b>) Young’s modulus in tension along the warp, (<b>c</b>) Interlaminar shear modulus, (<b>d</b>) Ultimate elongation along the base, (<b>e</b>) Ultimate elongation along the warp, (<b>f</b>) CTE, (<b>g</b>) Density with predictions made by the best architectures of the ANN (digits on yellow) and SVM (digits on cyan), architectures optimized using the MOPSO and NSGA-II algorithms, respectively.</p>
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14 pages, 4995 KiB  
Article
Laser-Sintering of Cyclic Olefine Copolymer for Low Dielectric Loss Applications
by Manuel Romeis, Michael Ehrngruber and Dietmar Drummer
Polymers 2024, 16(12), 1751; https://doi.org/10.3390/polym16121751 - 20 Jun 2024
Viewed by 1214
Abstract
With increasing demands for data transfer, the production of components with low dielectric loss is crucial for the development of advanced antennas, which are needed to meet the requirements of next-generation communication technologies. This study investigates the impact of a variation in energy [...] Read more.
With increasing demands for data transfer, the production of components with low dielectric loss is crucial for the development of advanced antennas, which are needed to meet the requirements of next-generation communication technologies. This study investigates the impact of a variation in energy density on the part properties of a low-loss cyclic olefin copolymer (COC) in the SLS process as a way to manufacture complex low-dielectric-loss structures. Through a systematic variation in the laser energy, its impact on the part density, geometric accuracy, surface quality, and dielectric properties of the fabricated parts is assessed. This study demonstrates notable improvements in material handling and the quality of the manufactured parts while also identifying areas for further enhancement, particularly in mitigating thermo-oxidative aging. This research not only underscores the potential of COC in the realm of additive manufacturing but also sets the stage for future studies aimed at optimizing process parameters and enhancing material formulations to overcome current limitations. Full article
(This article belongs to the Special Issue Progress in 3D Printing II)
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<p>Chemical structure of COC.</p>
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<p>ATR spectrum of (<b>a</b>) COC granulate and (<b>b</b>) COC samples manufactured at 10 W in the SLS process.</p>
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<p>(<b>a</b>) DSC and TGA (<b>b</b>) of Topaz COC Blend 16-024.</p>
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<p>(<b>a</b>) SEM of particles and (<b>b</b>) particle distribution.</p>
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<p>(<b>a</b>) Compression depth and (<b>b</b>) bulk density.</p>
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<p>Manufactured COC parts; line one: 10 W, 12 W, 14 W, 16 W (from <b>left</b> to <b>right</b>); line 2: 18 W, 20 W, 22 W, 24 W (from <b>left</b> to <b>right</b>).</p>
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<p>Part density (<b>a</b>) and surface roughness (<b>b</b>) of LS-COC parts.</p>
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<p>Dimensional accuracy: (<b>a</b>) length and (<b>b</b>) width/height of SLS-COC parts in dependence on laser power.</p>
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<p>(<b>a</b>) Relative permittivity and (<b>b</b>) dielectric loss tangent for different frequencies and laser intensities.</p>
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<p>(<b>a</b>) ATR measurements are dependent on laser intensities and (<b>b</b>) carbonyl index at 1750 cm<sup>−1</sup>.</p>
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<p>Carbonyl index of single layers at 1750 cm<sup>−1</sup>.</p>
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23 pages, 2968 KiB  
Review
Valorization of Grain and Oil By-Products with Special Focus on Hemicellulose Modification
by Xiaoxian Liu, Jin Xie, Nicolas Jacquet and Christophe Blecker
Polymers 2024, 16(12), 1750; https://doi.org/10.3390/polym16121750 - 20 Jun 2024
Viewed by 1034
Abstract
Hemicellulose is one of the most important natural polysaccharides in nature. Hemicellulose from different sources varies in chemical composition and structure, which in turn affects the modification effects and industrial applications. Grain and oil by-products (GOBPs) are important raw materials for hemicellulose. This [...] Read more.
Hemicellulose is one of the most important natural polysaccharides in nature. Hemicellulose from different sources varies in chemical composition and structure, which in turn affects the modification effects and industrial applications. Grain and oil by-products (GOBPs) are important raw materials for hemicellulose. This article reviews the modification methods of hemicellulose in GOBPs. The effects of chemical and physical modification methods on the properties of GOBP hemicellulose biomaterials are evaluated. The potential applications of modified GOBP hemicellulose are discussed, including its use in film production, hydrogel formation, three-dimensional (3D) printing materials, and adsorbents for environmental remediation. The limitations and future recommendations are also proposed to provide theoretical foundations and technical support for the efficient utilization of these by-products. Full article
(This article belongs to the Section Polymer Applications)
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<p>Representative chemical structures of hemicellulose ((<b>A</b>): Grasses, (<b>B</b>): Hardwood, (<b>C</b>): Softwood).</p>
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<p>The etherification of hemicellulose ((<b>A</b>): Carboxymethylation, (<b>B</b>): Methylation, (<b>C</b>): Benzylation, (<b>D</b>): Quaternization).</p>
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<p>The esterification of hemicellulose.</p>
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<p>Using two α-arabinofuranosidases to remove α-arabinofuranose from wheat xylan [<a href="#B76-polymers-16-01750" class="html-bibr">76</a>]. Copyright 2024. Reproduced with permission from the American Chemical Society.</p>
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<p>The synergistic enhancement of sodium alginate composite films by corn husk cellulose and hemicellulose [<a href="#B89-polymers-16-01750" class="html-bibr">89</a>]. Copyright 2024. Reproduced with permission from the Elsevier.</p>
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<p>Construction of fully bio-based hydrogels using cellulose nanocrystals and arabinoxylan (CNC: cellulose nanocrystals, AX: arabinoxylan) [<a href="#B104-polymers-16-01750" class="html-bibr">104</a>]. Copyright 2024. Reproduced with permission from the American Chemical Society.</p>
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<p>Synthesis of hemicellulose-co-PAAc hydrogels via radical copolymerization [<a href="#B105-polymers-16-01750" class="html-bibr">105</a>]. Copyright 2024. Reproduced with permission from the Elsevier.</p>
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<p>Laccase-induced cross-linking of xylan [<a href="#B51-polymers-16-01750" class="html-bibr">51</a>]. Copyright 2024. Reproduced with permission from the Elsevier.</p>
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16 pages, 16387 KiB  
Article
Process Characterizations of Ultrasonic Extruded Weld-Riveting of AZ31B Magnesium Alloy to Carbon Fiber-Reinforced PA66
by Zeguang Liu, Guanxiong Lu, Yuanduo Yang, Sansan Ao, Kaifeng Wang and Yang Li
Polymers 2024, 16(12), 1749; https://doi.org/10.3390/polym16121749 - 20 Jun 2024
Cited by 2 | Viewed by 943
Abstract
Traditional metal–plastic dissimilar welding methods directly heat the metal workpiece, which may cause potential thermal damage to the metal workpiece. Ultrasonic extruded weld-riveting (UEWR) is a relatively new method for dissimilar joining of carbon fiber-reinforced thermoplastic (CFRTP) and metal. In this method, the [...] Read more.
Traditional metal–plastic dissimilar welding methods directly heat the metal workpiece, which may cause potential thermal damage to the metal workpiece. Ultrasonic extruded weld-riveting (UEWR) is a relatively new method for dissimilar joining of carbon fiber-reinforced thermoplastic (CFRTP) and metal. In this method, the CFRTP workpiece is melted using the ultrasonic effect and is squeezed into prefabricated holes in the metal workpiece to form a rivet structure. In this method, the metal workpiece is not directly heated, and potential high-temperature losses can be avoided. This paper investigates the process characterizations of UERW of AZ31B magnesium alloy to carbon fiber-reinforced PA66. The process parameters are optimized by the Taguchi method. The joint formation process is analyzed based on the fiber distribution in the cross-sections of joints. The effects of welding parameters on the joint microstructure and fracture surface morphology are discussed. The results show that a stepped amplitude strategy (40 μm amplitude in the first stage and 56 μm amplitude in the second stage) could balance the joint strength and joint appearance. Insufficient (welding energy < 2600 J or amplitude-A < 50%) or excessive (welding energy > 2800 J or amplitude-A > 50%) welding parameters lead to the formation of porous defects. Three fracture modes are identified according to the fracture surface analysis. The maximum tensile shear strength of joints at the optimal parameters is about 56.5 ± 6.2 MPa. Full article
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<p>Three-dimensional display of the microstructure of the CF/PA66 sheet. “LD” indicates length direction (parallel with the injection direction), “TD” indicates transversal direction, and “T” indicates thickness direction.</p>
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<p>Schematic diagram of ultrasonic extruded weld-riveting process. (<b>a</b>) Schematic diagram of lap joint; (<b>b</b>) A magnesium alloy sheet with four prefabricated holes; (<b>c</b>) Anvil with a spherical concave zone; (<b>d</b>) A gird-type energy director.</p>
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<p>Schematic diagram of the ultrasonic extruded weld-riveting process. “Fw” means the welding force; “Fh” means the holding force.</p>
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<p>Main effect plot of process parameters on the mechanical property of the joint.</p>
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<p>Main effect plot of process parameters on the filling performance.</p>
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<p>Tensile shear strength with a single variable. (<b>a</b>) Welding energy as the variable while amplitude-A is fixed at 50%; (<b>b</b>) Amplitude-A as the variable while the welding energy is fixed at 2800 J.</p>
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<p>Cross-sectional microstructure at different parameters: (<b>a</b>–<b>e</b>) welding energies of 2400–3200 J while amplitude-A is fixed at 50%; (<b>f</b>–<b>j</b>) amplitude-A of 40%–80% when the welding energy is fixed at 2800 J.</p>
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<p>The typical morphologies of different defective areas. (<b>a</b>) loose area at 2400 J, 50% amplitude-A; (<b>b</b>) degradation area at 3000 J, 50% amplitude-A.</p>
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<p>The typical morphologies of porous areas. (<b>a</b>,<b>b</b>) 2800 J, 40% amplitude-A; (<b>c</b>,<b>d</b>) 2800 J, 60% amplitude-A; (<b>e</b>,<b>f</b>) 2800 J, 70% amplitude-A.</p>
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<p>The typical distribution of carbon fibers in the locations (<b>a</b>–<b>d</b>) of a joint when the welding energy is 2600 J and amplitude-A is 50%.</p>
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<p>The hole-filling process in UEWR.</p>
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<p>Typical fracture surfaces of a joint: (<b>a</b>) macroscopic view; (<b>b</b>)magnified contour of a single-hole fracture surface.</p>
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<p>Interfacial fracture modes of typical joints. (<b>a</b>) 2400 J, 50% amplitude-A; (<b>b</b>) 2800 J, 50% amplitude-A.</p>
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<p>Fracture surface morphologies at various welding parameters: (<b>a</b>) 2400 J, 50% amplitude-A; (<b>b</b>) 2600 J, 50% amplitude-A; (<b>c</b>) 2800 J, 50% amplitude-A; (<b>d</b>) 3000 J, 50% amplitude-A; (<b>e</b>) 3200 J, 50% amplitude-A; (<b>f</b>) 2800 J, 40% amplitude-A; (<b>g</b>) 2800 J, 50% amplitude-A; (<b>h</b>) 2800 J, 60% amplitude-A; (<b>i</b>) 2800 J, 70% amplitude-A; (<b>j</b>) 2800 J, 80% amplitude-A.</p>
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<p>Fiber–matrix debonding fracture surface morphology.</p>
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16 pages, 2636 KiB  
Article
Characterization of a Delivery System Based on a Hyaluronic Acid 3D Scaffold and Gelatin Microparticles
by Cristina Martínez-Ramos, Alejandro Rodríguez Ruiz, Manuel Monleón Pradas and Fernando Gisbert Roca
Polymers 2024, 16(12), 1748; https://doi.org/10.3390/polym16121748 - 20 Jun 2024
Viewed by 4063
Abstract
The objective of this study was to develop and characterize a novel hyaluronic acid (HA) 3D scaffold integrated with gelatin microparticles for sustained-delivery applications. To achieve this goal, the delivery microparticles were synthesized and thoroughly characterized, focusing on their crosslinking mechanisms (vanillin and [...] Read more.
The objective of this study was to develop and characterize a novel hyaluronic acid (HA) 3D scaffold integrated with gelatin microparticles for sustained-delivery applications. To achieve this goal, the delivery microparticles were synthesized and thoroughly characterized, focusing on their crosslinking mechanisms (vanillin and genipin), degradation profiles, and release kinetics. Additionally, the cytotoxicity of the system was assessed, and its impact on the cell adhesion and distribution using mouse fibroblasts was examined. The combination of both biomaterials offers a novel platform for the gradual release of various factors encapsulated within the microparticles while simultaneously providing cell protection, support, and controlled factor dispersion due to the HA 3D scaffold matrix. Hence, this system offers a platform for addressing injure repair by continuously releasing specific encapsulated factors for optimal tissue regeneration. Additionally, by leveraging the properties of HA conjugates with small drug molecules, we can enhance the solubility, targeting capabilities, and cellular absorption, as well as prolong the system stability and half-life. As a result, this integrated approach presents a versatile strategy for therapeutic interventions aimed at promoting tissue repair and regeneration. Full article
(This article belongs to the Section Biobased and Biodegradable Polymers)
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<p>SEM and fluorescence microscope images of the combined structure. SEM was used to study the structure of the HA scaffold with the gelatin microparticles crosslinked with genipin (images (<b>A</b>–<b>D</b>)) at 5×, 30×, 600×, and 2000×, respectively. Images (<b>E</b>,<b>F</b>) show the distribution of gelatin microparticles crosslinked with genipin and loaded with BSA-FITC in the HA scaffold once vacuum-injected at 10× and 20×, respectively.</p>
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<p>SEM images of the gelatin microparticles. SEM was used to image the dry morphologies of gelatin microparticles before crosslinking (<b>A</b>) and after crosslinking with vanilin (<b>B</b>) and genipin (<b>C</b>).</p>
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<p>Release of BSA and diffusion coefficients of microparticles. Percentage of BSA released in the 3 studied groups of microparticles: without crosslinking, crosslinked with genipin, and crosslinked with vanilin. A linear stage is observed during the first 4–5 h, followed by a saturation phase, as the group of microparticles crosslinked with genipin is the one that released the greatest amount of BSA.</p>
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<p>Degradation study of microparticles. SEM pictures of the microparticle morphologies without crosslinking (<b>A</b>), crosslinked with vanilin (<b>B</b>), and crosslinked with genipin (<b>C</b>), showing less degradation on the genipin-crosslinked microparticles. Degradation of microparticles after 24, 72, and 144 h (<b>D</b>), confirming the lesser degradation of the genipin-crosslinked microparticles. Statistically significant differences are indicated by *** and ****, indicating <span class="html-italic">p</span>-values below 0.001 and 0.0001, respectively.</p>
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<p>Cell viabilities via MTT assay after 24 h, 48 h, and 72 h. Cytotoxicity by indirect contact (extracts) of the negative control (NC), positive control (PC), and genipin-crosslinked gelatin microspheres on HA scaffold (HA–gelatin) using mouse fibroblast cells (L929). If the cell viability of the sample is &gt;70%, the material shall be considered non-cytotoxic (dotted line). Statistically significant differences are indicated by *, *** and ****, indicating <span class="html-italic">p</span>-values below 0.05, 0.001 and 0.0001, respectively.</p>
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<p>Confocal and scanning electron microscope (SEM) images of L929 cells cultured for 7 days on the system. In the confocal images (<b>A</b>,<b>B</b>), the attachment of the L929 cells to the scaffold of HA with gelatin microparticles crosslinked with genipin can be observed. In the SEM images (<b>C</b>,<b>D</b>), micrographs of fibroblasts cultured on the system are observed, showing the complete cell coverage of the HA scaffold with gelatin microparticles.</p>
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18 pages, 9168 KiB  
Article
Dual-Mode Ce-MOF Nanozymes for Rapid and Selective Detection of Hydrogen Sulfide in Aquatic Products
by Qi Cheng, Xiaoyu Du, Zuyao Fu, Zhaoyang Ding and Jing Xie
Polymers 2024, 16(12), 1747; https://doi.org/10.3390/polym16121747 - 20 Jun 2024
Cited by 1 | Viewed by 1503
Abstract
Increasing concern over the safety of consumable products, particularly aquatic products, due to freshness issues, has become a pressing issue. Therefore, ensuring the quality and safety of aquatic products is paramount. To address this, a dual-mode colorimetric–fluorescence sensor utilizing Ce-MOF as a mimic [...] Read more.
Increasing concern over the safety of consumable products, particularly aquatic products, due to freshness issues, has become a pressing issue. Therefore, ensuring the quality and safety of aquatic products is paramount. To address this, a dual-mode colorimetric–fluorescence sensor utilizing Ce-MOF as a mimic peroxidase to detect H2S was developed. Ce-MOF was prepared by a conventional solvothermal synthesis method. Ce-MOF catalyzed the oxidation of 3,3’,5,5’-tetramethylbenzidine (TMB) by hydrogen peroxide (H2O2) to produce blue oxidized TMB (oxTMB). When dissolved, hydrogen sulfide (H2S) was present in the solution, and it inhibited the catalytic effect of Ce-MOF and caused the color of the solution to fade from blue to colorless. This change provided an intuitive indication for the detection of H2S. Through steady-state dynamic analysis, the working mechanism of this sensor was elucidated. The sensor exhibited pronounced color changes from blue to colorless, accompanied by a shift in fluorescence from none to light blue. Additionally, UV–vis absorption demonstrated a linear correlation with the H2S concentration, ranging from 200 to 2300 µM, with high sensitivity (limit of detection, LOD = 0.262 μM). Fluorescence intensity also showed a linear correlation, ranging from 16 to 320 µM, with high selectivity and sensitivity (LOD = 0.156 μM). These results underscore the sensor’s effectiveness in detecting H2S. Furthermore, the sensor enhanced the accuracy of H2S detection and fulfilled the requirements for assessing food freshness and safety. Full article
(This article belongs to the Special Issue Application of Metal-Organic Frameworks Based on Polymers)
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<p>Morphology of Ce-MOF: (<b>a</b>) SEM image; (<b>b</b>) TEM image; (<b>c</b>) DLS analysis; (<b>d</b>) EDS images.</p>
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<p>Characterization of Ce-MOF: (<b>a</b>) XRD spectra; (<b>b</b>) FT-IR spectra; (<b>c</b>) Nitrogen adsorption–desorption isotherm; (<b>d</b>) BJH pore diameter; (<b>e</b>) XPS spectra; (<b>f</b>) C 1s spectra; (<b>g</b>) O 1s spectra; (<b>h</b>) Ce 3d spectra.</p>
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<p>Steady-state kinetic analysis: (<b>a</b>,<b>b</b>) Kinetic study for the substrate of H<sub>2</sub>O<sub>2</sub> of Ce-MOF based on the Michaelis–Menten equation; (<b>c</b>,<b>d</b>) Kinetic study for the substrate of TMB of Ce-MOF based on the Michaelis–Menten equation.</p>
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<p>Colorimetric characteristic analysis: (<b>a</b>) Feasibility of colorimetric detection of dual-mode sensor; (<b>b</b>) EPR spectrum of DMPO- OH.</p>
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<p>Dual-mode colorimetric–fluorescence sensor responds to different H<sub>2</sub>S concentrations: (<b>a</b>) Linear relationship between UV–vis absorption and different H<sub>2</sub>S concentrations; (<b>b</b>) Fluorescence spectrum of different H<sub>2</sub>S concentrations under excitation of 325 nm; (<b>c</b>) Linear relationship between fluorescence spectrum and different H<sub>2</sub>S concentrations; (<b>d</b>) Fluorescence lifetime of Ce-MOF.</p>
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<p>Selectivity and anti-interference of Ce-MOF: (<b>a</b>) UV–vis absorption spectrum from the responses of Ce-MOF in the presence of H<sub>2</sub>S or coexistence with other species; (<b>b</b>) Fluorescence intensity from the responses of Ce-MOF in the presence of H<sub>2</sub>S or coexistence with other species.</p>
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<p>Application of Ce-MOF in real samples: (<b>a</b>) H<sub>2</sub>S detection in shrimp; (<b>b</b>) H<sub>2</sub>S detection in salmon.</p>
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<p>Schematic representation of the preparation of Ce-MOF and the colorimetric–fluorescent sensing of H<sub>2</sub>S.</p>
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22 pages, 5171 KiB  
Article
Flash Pyrolysis of Waste Tires in an Entrained Flow Reactor—An Experimental Study
by Balan Ramani, Arqam Anjum, Eddy Bramer, Wilma Dierkes, Anke Blume and Gerrit Brem
Polymers 2024, 16(12), 1746; https://doi.org/10.3390/polym16121746 - 20 Jun 2024
Cited by 1 | Viewed by 2027
Abstract
In this study, a flash pyrolysis process is developed using an entrained flow reactor for recycling of waste tires. The flash pyrolysis system is tested for process stability and reproducibility of the products under similar operating conditions when operated continuously. The study is [...] Read more.
In this study, a flash pyrolysis process is developed using an entrained flow reactor for recycling of waste tires. The flash pyrolysis system is tested for process stability and reproducibility of the products under similar operating conditions when operated continuously. The study is performed with two different feedstock materials, i.e., passenger car (PCT) and truck tire (TT) granulates, to understand the influence of feedstock on the yield and properties of the pyrolysis products. The different pyrolytic products i.e., pyrolytic carbon black (pCB), oil, and pyro-gas, are analyzed, and their key properties are discussed. The potential applications for the obtained pyrolytic products are discussed. Finally, a mass and energy balance analysis has been performed for the developed pyrolysis process. The study provides insight into the governing mechanisms of the flash pyrolysis process for waste tires, which is useful to optimize the process depending on the desired applications for the pyrolysis products, and also to scale up the pyrolysis process. Full article
(This article belongs to the Special Issue Recycling of Plastic and Rubber Wastes)
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<p>Schematic of the waste tire pyrolysis process with product applications.</p>
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<p>Particle size distribution of the feed tire particles: (<b>a</b>) passenger car tire; (<b>b</b>) truck tire.</p>
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<p>Schematic drawing of the entrained flow reactor experimental setup.</p>
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<p>(<b>a</b>) Temperature profiles at different positions in the entrained flow pyrolysis setup, (<b>b</b>) pressure profiles at reactor inlet and at the exhaust of the setup, and (<b>c</b>) gas flow rate profile during a continuous pyrolysis production run.</p>
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<p>Thermogravimetric analysis of waste tires used: PCT; TT.</p>
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<p>DTG/TGA curves of volatiles: PCT; TT.</p>
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<p>Product yields for two different feedstocks: (<b>a</b>) PCT; (<b>b</b>) TT. * Measured by difference, i.e., gas = 100—solid—liquid (in wt. %).</p>
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<p>SEM images of pCB particles—PCT (<b>a</b>–<b>c</b>); TT (<b>d</b>–<b>f</b>).</p>
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<p>Particle size distribution for pCBs from PCT and TT feedstocks: (<b>a</b>) primary particles; (<b>b</b>) agglomerates.</p>
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<p>Schematic diagram of the afterburner analyzer.</p>
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<p>Elemental balances (C, H, N, S) of the flash pyrolysis process for PCT (<b>a</b>–<b>d</b>) and TT (<b>e</b>–<b>h</b>) feedstocks. * Measured by difference for the pyro-gas (i.e., pyro-gas = tire—pCB—oil) in wt. %.</p>
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<p>Energy balance of the flash pyrolysis process for (<b>a</b>) PCT and (<b>b</b>) TT feedstocks. * Measured by difference for the pyro-gas (i.e., pyro-gas = tire—pCB—oil).</p>
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12 pages, 916 KiB  
Article
Development of a Biopolymer-Based Anti-Fog Coating with Sealing Properties for Applications in the Food Packaging Sector
by Masoud Ghaani, Maral Soltanzadeh, Daniele Carullo and Stefano Farris
Polymers 2024, 16(12), 1745; https://doi.org/10.3390/polym16121745 - 20 Jun 2024
Viewed by 1563
Abstract
The quest for sustainable and functional food packaging materials has led researchers to explore biopolymers such as pullulan, which has emerged as a notable candidate for its excellent film-forming and anti-fogging properties. This study introduces an innovative anti-fog coating by combining pullulan with [...] Read more.
The quest for sustainable and functional food packaging materials has led researchers to explore biopolymers such as pullulan, which has emerged as a notable candidate for its excellent film-forming and anti-fogging properties. This study introduces an innovative anti-fog coating by combining pullulan with poly (acrylic acid sodium salt) to enhance the display of packaged food in high humidity environments without impairing the sealing performance of the packaging material—two critical factors in preserving food quality and consumers’ acceptance. The research focused on varying the ratios of pullulan to poly (acrylic acid sodium salt) and investigating the performance of this formulation as an anti-fog coating on bioriented polypropylene (BOPP). Contact angle analysis showed a significant improvement in BOPP wettability after coating deposition, with water contact angle values ranging from ~60° to ~17° for formulations consisting only of poly (acrylic acid sodium salt) (P0) or pullulan (P100), respectively. Furthermore, seal strength evaluations demonstrated acceptable performance, with the optimal formulation (P50) achieving the highest sealing force (~2.7 N/2.5 cm) at higher temperatures (130 °C). These results highlight the exceptional potential of a pullulan-based coating as an alternative to conventional packaging materials, significantly enhancing anti-fogging performance. Full article
(This article belongs to the Special Issue Development and Application of Bio-Based Polymers)
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<p>(<b>A</b>) Comparison between theoretical and experimental coating thicknesses for samples P0, P25, P50, P75, and P100. (<b>B</b>) Percentage variation between theoretical and experimental coating thicknesses for the different samples.</p>
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<p>Seal strength comparison at various temperatures for samples P0, P25, P50, P75, and P100.</p>
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<p>Water contact angle of (<b>a</b>) polypropylene film neutral (no surface treatment); (<b>b</b>) anti-fog coating (formulation P100) immediately after depositing the water droplet; (<b>c</b>) anti-fog coating (formulation P100) after ~10 s of depositing the water droplet.</p>
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<p>Normalised haze percentages at 1 µm coating thickness for samples P0, P25, P50, P75, and P100.</p>
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20 pages, 10437 KiB  
Article
The Seed Germination Test as a Valuable Tool for the Short-Term Phytotoxicity Screening of Water-Soluble Polyamidoamines
by Elisabetta Ranucci, Sofia Treccani, Paolo Ferruti and Jenny Alongi
Polymers 2024, 16(12), 1744; https://doi.org/10.3390/polym16121744 - 19 Jun 2024
Cited by 1 | Viewed by 1534
Abstract
Six differently charged amphoteric polyamidoamines, synthesized by the polyaddition of N,N′-methylenebisacrylamide to alanine, leucine, serine, arginine (M-ARG), glutamic acid (M-GLU) and a glycine/cystine mixture, were screened for their short-term phytotoxicity using a seed germination test. Lepidium sativum L. seeds were [...] Read more.
Six differently charged amphoteric polyamidoamines, synthesized by the polyaddition of N,N′-methylenebisacrylamide to alanine, leucine, serine, arginine (M-ARG), glutamic acid (M-GLU) and a glycine/cystine mixture, were screened for their short-term phytotoxicity using a seed germination test. Lepidium sativum L. seeds were incubated in polyamidoamine water solutions with concentrations ranging from 0.156 to 2.5 mg mL−1 at 25 ± 1 °C for 120 h. The seed germination percentage (SG%), an indicator of acute toxicity, and both root and shoot elongation, related to plant maturation, were the considered endpoints. The germination index (GI) was calculated as the product of relative seed germination times relative radical growth. The SG% values were in all cases comparable to those obtained in water, indicating no detectable acute phytotoxicity of the polyamidoamines. In the short term, the predominantly positively charged M-ARG proved to be phytotoxic at all concentrations (GI < 0.8), whereas the predominantly negatively charged M-GLU proved to be biostimulating at intermediate concentrations (GI > 1) and slightly inhibitory at 2.5 mg mL−1 (0.8 < GI < 1). Overall, polyamidoamine phytotoxicity could be correlated to charge distribution, demonstrating the potential of the test for predicting and interpreting the eco-toxicological behavior of water-soluble polyelectrolytes. Full article
(This article belongs to the Section Polymer Applications)
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<p>Ionic species distribution of α-amino acid-derived PAAs at pH 7.0, except for M-GLY<sub>50</sub>-CYSS<sub>50</sub>, for which the pH considered is 7.5. In the case of the M-GLY<sub>50</sub>-CYSS<sub>50</sub> copolymer, the repeating units M-GLY and M-CYSS are considered separately. The PAA codes are specified in <a href="#polymers-16-01744-t001" class="html-table">Table 1</a>.</p>
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<p>Water uptake during the phases of seed germination (<b>a</b>). Morphology of <span class="html-italic">Lepidium sativum</span> L. seeds at different stages of the germination process (<b>b</b>).</p>
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<p>Germination kinetics of <span class="html-italic">Lepidium sativum</span> L. seeds exposed to 2.5 mg mL<sup>−1</sup> PAA solutions for 24 h in sunlight at 25 ± 1 °C (<b>a</b>). Time to rupture of testa tegument (<b>b</b>). Time to seed germination, identified as the protrusion of a 2 mm radicle. The time to maximum imbibition was 2 h ± 0.5 in all cases. The collected values are reported as the average of three measurements plus their standard deviation.</p>
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<p><span class="html-italic">Lepidium sativum</span> L. seedling growth after seed exposure to deionized water at 0 (<b>a</b>) and 120 h (<b>b</b>). Optical microscope image of seedlings grown in deionized water (<b>c</b>). Effect of seed exposure to the positive control (0.1% K<sub>2</sub>Cr<sub>2</sub>O<sub>7</sub>) at 0 h (<b>d</b>) and 120 h (<b>e</b>).</p>
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<p><span class="html-italic">Lepidium sativum</span> L. seedling growth after seed exposure to 2.5 mg mL<sup>−1</sup> PAA solutions for 120 h.</p>
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<p>Concentration dependence of the seed germination percentage, SG%, of <span class="html-italic">Lepidium sativum</span> L. seeds exposed to PAA solutions for 120 h (colored bars). For each PAA concentration, tests were conducted in quadruplicate in parallel to tests performed on an equal number of seeds incubated in water, taken as the negative control (blue bars).</p>
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<p>Concentration dependence of the relative seed germination (RSG) of <span class="html-italic">Lepidium sativum</span> L. seeds exposed to PAA solutions for 120 h. The black dashed line represents <span class="html-italic">RSG</span> = 1 corresponding to an equal number of seeds germinated in the test sample and in water.</p>
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<p>Concentration dependence of the length of <span class="html-italic">Lepidium sativum</span> L. roots after seed incubation in PAA aqueous solutions for 120 h (colored bars). For each PAA concentration, tests were conducted in quadruplicate in parallel to tests performed on an equal number of seeds incubated in water, which were taken as the negative control (blue bars). The results are reported as the mean ± confidence. Asterisks indicate significant differences (<span class="html-italic">p</span>-value &lt; 0.05) compared to the control: the black asterisks indicate a greater length in water, the green asterisks a greater length in the PAA solution.</p>
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<p>Concentration dependence of the length of <span class="html-italic">Lepidium sativum</span> L. shoots after seed incubation in PAA aqueous solutions for 120 h (colored bars). For each PAA concentration, tests were conducted in quadruplicate in parallel to tests performed on an equal number of seeds incubated in water, which were taken as the negative control (blue bars). The results are reported as the mean ± confidence. Asterisks indicate significant differences (<span class="html-italic">p</span>-value &lt; 0.05) compared to the control: black asterisks indicate a greater length in water, and green asterisks a greater length in the PAA solution.</p>
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<p>Concentration dependence of the relative radicle growth of <span class="html-italic">Lepidium sativum</span> L. seedlings in PAA water solutions after 120 h. The results are reported as the mean ± confidence. The black dashed line represents <span class="html-italic">RRG</span> = 1 corresponding to an equal radicle length in the test sample and in water.</p>
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<p>Concentration dependence of the germination index of <span class="html-italic">Lepidium sativum</span> L. seeds exposed to PAA water solutions for 120 h. The red (<span class="html-italic">GI</span> = 0.5), black (<span class="html-italic">GI</span> = 0.8) and green (<span class="html-italic">GI</span> = 1.0) dashed lines represent threshold values of different phytotoxic levels. In detail: <span class="html-italic">GI</span> &lt; 0.5 corresponds to high phytotoxicity; 0.5 &lt; <span class="html-italic">GI</span> &lt; 0.8 corresponds to moderate phytotoxicity; 0.8 &lt; <span class="html-italic">GI</span> &lt; 1 corresponds to moderate inhibitory effect; <span class="html-italic">GI</span> &gt; 1 corresponds to phytostimulation.</p>
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<p>General synthesis of linear polyamidoamines.</p>
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<p>Synthesis of PAA homopolymers (<b>a</b>) and of the glycine–cystine-derived PAA copolymer (<b>b</b>). For the sake of simplicity, charges have been omitted.</p>
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19 pages, 5651 KiB  
Article
Advanced Dentistry Biomaterials Containing Graphene Oxide
by Doina Prodan, Marioara Moldovan, Stanca Cuc, Codruţa Sarosi, Ioan Petean, Miuța Filip, Rahela Carpa, Rami Doukeh and Ioana-Codruta Mirica
Polymers 2024, 16(12), 1743; https://doi.org/10.3390/polym16121743 - 19 Jun 2024
Viewed by 1172
Abstract
The aim of this study was to obtain three experimental resin-based cements containing GO and HA-Ag for posterior restorations. The samples (S0, S1, and S2) shared the same polymer matrix (BisGMA, TEGDMA) and powder mixture (bioglass (La2O3 and Sr-Zr), quartz, [...] Read more.
The aim of this study was to obtain three experimental resin-based cements containing GO and HA-Ag for posterior restorations. The samples (S0, S1, and S2) shared the same polymer matrix (BisGMA, TEGDMA) and powder mixture (bioglass (La2O3 and Sr-Zr), quartz, GO, and HA-Ag), with different percentages of graphene oxide (0%, 0.1%, 0.2% GO) and silver-doped hydroxyapatite (10%, 9.9%, 9.8% HA-Ag). The physical–chemical properties (water absorption, degree of conversion), mechanical properties (DTS, CS, FS), structural properties (SEM, AFM), and antibacterial properties (Staphylococcus aureus, Enterococcus faecalis, Streptococcus mutans, Porphyromonas gingivalis, and Escherichia coli) were investigated. The results showed that the mechanical properties, except for the diametral tensile test, increased with the rise in the %GO. After 28 days, water absorption increased with the rise in the %GO. The surface structure of the samples did not show major changes after water absorption for 28 days. The antibacterial effects varied depending on the samples and bacterial strains tested. After increasing the %GO and decreasing the %HA-Ag, we observed a more pronounced antibacterial effect. The presence of GO, even in very small percentages, improved the properties of the tested experimental cements. Full article
(This article belongs to the Special Issue Functional Graphene-Polymer Composites)
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<p>The bacterial strains studied and the samples (S0, S1, and S2) tested (Sa—<span class="html-italic">Staphylococcus aureus</span>, Ec—<span class="html-italic">Escherichia coli</span>, Ef—<span class="html-italic">Enterococcus faecalis</span>, Pg—<span class="html-italic">Porphyromonas gingivalis</span>, Sm—<span class="html-italic">Streptococcus mutans</span>).</p>
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<p>The degree of conversion of the liquid sample and of the cement samples immediately cured and 24 h after polymerization.</p>
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<p>Stress–strain curves for the mechanical tests.</p>
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<p>Water absorption of sample S0 (without GO) and samples S1 and S2 (with 0.1% and 2% GO, respectively) after 1, 2, 3, 7, 10, 14, 21, and 28 days.</p>
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<p>SEM images on the surface of samples S0 (<b>a</b>,<b>d</b>), S1 (<b>b</b>,<b>e</b>), and S2 (<b>c</b>,<b>f</b>) before the water absorption test (<b>a</b>–<b>c</b>) and after 28 days of storage in water (<b>d</b>–<b>f</b>).</p>
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<p>AFM images of the samples’ fine microstructures before liquid immersion: (<b>a</b>) S0, (<b>b</b>) S1, (<b>c</b>) S2 and after liquid immersion for 28 days: (<b>d</b>) S0, (<b>e</b>) S1, and (<b>f</b>) S2.</p>
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<p>AFM images of the sample’s nanostructure before liquid immersion: (<b>a</b>) S0, (<b>b</b>) S1, (<b>c</b>) S2 and after liquid immersion for 28 days: (<b>d</b>) S0, (<b>e</b>) S1, (<b>f</b>) S2.</p>
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<p>Surface roughness variation for the (<b>a</b>) fine microstructure and (<b>b</b>) nanostructure.</p>
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<p>Antibacterial activity of the cement samples (S0, S1, S2), after 48 h of incubation against Sa—<span class="html-italic">Staphylococcus aureus</span>, Ec—<span class="html-italic">Escherichia coli</span>, Ef—<span class="html-italic">Enterococcus faecalis</span>, Pg—<span class="html-italic">Porphyromonas gingivalis</span>, Sm—<span class="html-italic">Streptococcus mutans</span>.</p>
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16 pages, 4487 KiB  
Article
An Oxalato-Bridged Cu(II)-Based 1D Polymer Chain: Synthesis, Structure, and Adsorption of Organic Dyes
by Fouzia Munawar, Muhammad Khalid, Muhammad Imran, Muhammad Naveed Qasim, Shazia Waseem, Murad A. AlDamen, Muhammad Ashfaq, Muhammad Imran and Muhammad Nadeem Akhtar
Polymers 2024, 16(12), 1742; https://doi.org/10.3390/polym16121742 - 19 Jun 2024
Cited by 1 | Viewed by 932
Abstract
In the current research, we prepared a polymeric framework, {[Cu(C2O4)(C10H8N2)]·H2O·0.67(CH3OH)]}n (1) (where C2O4 = oxalic acid; C10H8N2 = [...] Read more.
In the current research, we prepared a polymeric framework, {[Cu(C2O4)(C10H8N2)]·H2O·0.67(CH3OH)]}n (1) (where C2O4 = oxalic acid; C10H8N2 = 2,2-bipyridine), and explored this compound for adsorption of methylene blue (MB) and methyl orange (MO). The crystal structure of the compound consists of a Cu(ox)(bpy) unit connected via oxalate to form a 1D polymeric chain. This polymeric chain has adsorption capacities of 194.0 and 167.3 mg/g for MB and MO, respectively. The removal rate is estimated to be 77.6% and 66.9% for MB and MO, respectively. The plausible mechanisms for adsorption are electrostatic, π-π interaction, and OH-π interaction for dye stickiness. The adsorbent surface exhibits a negative charge that produces the electrostatic interaction, resulting in excellent adsorption efficiency at pH 7 and 8. The pseudo-first-order kinetic model is selected for the adsorption of MB and MO on the adsorbent. The reported compound has remarkable efficiency for sorption of organic dyes and can be useful in wastewater treatment. Full article
(This article belongs to the Section Polymer Chemistry)
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<p>Structural representation of MB dye.</p>
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<p>Structural representation of MO dye.</p>
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<p>(<b>a</b>) Labeled ball-and-stick of the asymmetric unit of <b>1</b>; (<b>b</b>) ORTEP diagram of <b>1</b> showing the polymeric 1D- chain formed along a-axis.</p>
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<p>(<b>a</b>) Contact time effect on the % age removal efficiency and (<b>b</b>) on adsorption ability of dyes; (<b>c</b>) Initial concentration effect of dyes on % age removal efficiency and (<b>d</b>) on adsorption ability of the dyes.</p>
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<p>(<b>a</b>) Effect of pH and (<b>b</b>) effect of adsorbent on adsorption capacity of dyes; (<b>c</b>) Effect of temperature on adsorption capacity; and (<b>d</b>) on % age efficiency of dyes.</p>
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<p>(<b>a</b>) Pseudo-first-order kinetic model fitted for MB; (<b>b</b>) pseudo-first-order kinetic model fitted for MO; (<b>c</b>) pseudo-second-order kinetic model fitted for MB; (<b>c</b>) pseudo-second-order kinetic model fitted for MB.</p>
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<p>(<b>a</b>) Freundlich adsorption isotherm fitted for MB; (<b>b</b>) Freundlich adsorption isotherm fitted for MO; (<b>c</b>) Langmuir adsorption isotherm fitted for MB; (<b>d</b>) Langmuir adsorption isotherm fitted for MO.</p>
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<p>Recyclability of adsorbent <b>1.</b></p>
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<p>Liquid film diffusion kinetic model fitting.</p>
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<p>Possible mechanism of cationic/anionic dye adsorption for <b>1</b>.</p>
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17 pages, 6621 KiB  
Article
New Fire-Retardant Open-Cell Composite Polyurethane Foams Based on Triphenyl Phosphate and Natural Nanoscale Additives
by Kirill Cherednichenko, Egor Smirnov, Maria Rubtsova, Dmitrii Repin and Anton Semenov
Polymers 2024, 16(12), 1741; https://doi.org/10.3390/polym16121741 - 19 Jun 2024
Cited by 1 | Viewed by 1191
Abstract
Despite the mechanical and physical properties of polyurethane foams (PUF), their application is still hindered by high inflammability. The elaboration of effective, low-cost, and environmentally friendly fire retardants remains a pressing issue that must be addressed. This work aims to show the feasibility [...] Read more.
Despite the mechanical and physical properties of polyurethane foams (PUF), their application is still hindered by high inflammability. The elaboration of effective, low-cost, and environmentally friendly fire retardants remains a pressing issue that must be addressed. This work aims to show the feasibility of the successful application of natural nanomaterials, such as halloysite nanotubes and nanocellulose, as promising additives to the commercial halogen-free, fire-retardant triphenyl phosphate (TPP) to enhance the flame retardance of open-cell polyurethane foams. The nanocomposite foams were synthesized by in situ polymerization. Investigation of the mechanical properties of the nanocomposite PUF revealed that the nanoscale additives led to a notable decrease in the foam’s compressibility. The obtained results of the flammability tests clearly indicate that there is a prominent synergetic effect between the fire-retardant and the natural nanoscale additives. The nanocomposite foams containing a mixture of TPP (10 and 20 parts per hundred polyol by weight) and either 10 wt.% of nanocellulose or 20 wt.% of halloysite demonstrated the lowest burning rate without dripping and were rated as HB materials according to UL 94 classification. Full article
(This article belongs to the Special Issue Advances in Functional Polyurethane and Composites)
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<p>SEM micrographs, elemental mapping and the corresponding EDS spectrum of PUF/20HNT (<b>A</b>), PUF/20TPP (<b>B</b>), and PUF/20TPP/20HNT (<b>C</b>).</p>
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<p>The photos of the cross sections, apparent densities, and box-plots of the cell area of PUF/TPP/HNT and PUF/TPP/NC.</p>
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<p>(<b>A</b>) FTIR spectra of individual HNT, TPP, reference PUF, PUF/20TPP, PUF/20HNT, and PUF/20TPP/20HNT; (<b>B</b>) FTIR spectra of individual NC, TPP, reference PUF, PUF/20TPP, PUF/20NC, and PUF/20TPP/20NC. The red, blue, and green dashed zones indicate the presence of TPP, HNT, and NC bands in the FTIR spectra of the final nanocomposite PUF samples, respectively.</p>
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<p>Results of compression force deflection measurements for the reference PUF, PUF modified with 10 php and 20 php of TPP and nanocomposite PUF: (<b>A</b>) PUF/10TPP/HNT and PUF/20TPP/HNT, (<b>B</b>) PUF/10TPP/NC and PUF/20TPP/NC.</p>
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<p>dTG curves of reference PUF, single TPP, PUF modified with 10 php and 20 php of TPP, and nanocomposite PUF: (<b>A</b>) PUF/TPP10/HNT, (<b>B</b>) PUF/TPP20/HNT, (<b>C</b>) PUF/TPP10/NC, and (<b>D</b>) PUF/TPP20/NC.</p>
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<p>Burning rates of PUF/TPP/HNT (<b>A</b>) and PUF/TPP/NC (<b>B</b>) in comparison with reference PUF, foams modified with 10 and 20 php of TPP and 10 and 20 wt.% of HNT and NC. The horizontal dashed line represents burning rate of 40 mm/min, which corresponds to HB class.</p>
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<p>SEM micrographs of char layer and the corresponding EDS spectra of PUF/20HNT, PUF/20NC, PUF/20TPP, PUF/20TPP/20HNT, and PUF/20TPP/20NC. The zones of sample analyzed at higher magnification and zones of EDS analysis are marked by green and red, respectively.</p>
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15 pages, 9036 KiB  
Review
Substrate Neutrality for Obtaining Block Copolymer Vertical Orientation
by Kaitlyn Hillery, Nayanathara Hendeniya, Shaghayegh Abtahi, Caden Chittick and Boyce Chang
Polymers 2024, 16(12), 1740; https://doi.org/10.3390/polym16121740 - 19 Jun 2024
Viewed by 1218
Abstract
Nanopatterning methods utilizing block copolymer (BCP) self-assembly are attractive for semiconductor fabrication due to their molecular precision and high resolution. Grafted polymer brushes play a crucial role in providing a neutral surface conducive for the orientational control of BCPs. These brushes create a [...] Read more.
Nanopatterning methods utilizing block copolymer (BCP) self-assembly are attractive for semiconductor fabrication due to their molecular precision and high resolution. Grafted polymer brushes play a crucial role in providing a neutral surface conducive for the orientational control of BCPs. These brushes create a non-preferential substrate, allowing wetting of the distinct chemistries from each block of the BCP. This vertically aligns the BCP self-assembled lattice to create patterns that are useful for semiconductor nanofabrication. In this review, we aim to explore various methods used to tune the substrate and BCP interface toward a neutral template. This review takes a historical perspective on the polymer brush methods developed to achieve substrate neutrality. We divide the approaches into copolymer and blended homopolymer methods. Early attempts to obtain neutral substrates utilized end-grafted random copolymers that consisted of monomers from each block. This evolved into side-group-grafted chains, cross-linked mats, and block cooligomer brushes. Amidst the augmentation of the chain architecture, homopolymer blends were developed as a facile method where polymer chains with each chemistry were mixed and grafted onto the substrate. This was largely believed to be challenging due to the macrophase separation of the chemically incompatible chains. However, innovative methods such as sequential grafting and BCP compatibilizers were utilized to circumvent this problem. The advantages and challenges of each method are discussed in the context of neutrality and feasibility. Full article
(This article belongs to the Special Issue Block Copolymers: Synthesis, Self-Assembly and Application)
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<p>Schematic of nanofabrication process of chemically patterned substrates [<a href="#B29-polymers-16-01740" class="html-bibr">29</a>] highlighting the direct assembly of a BCP process using various forms of neutrality: (<b>a</b>) homopolymer brushes; (<b>b</b>) mixed homopolymer brushes; (<b>c</b>) random copolymer brushes; (<b>d</b>) side-chain brushes; (<b>e</b>) ternary homopolymer brushes; (<b>f</b>) cross-linked polymer mats; (<b>g</b>) block cooligomer brushes. Colors represent polymers with distinct repeat units. Adapted with permission from references [<a href="#B1-polymers-16-01740" class="html-bibr">1</a>,<a href="#B29-polymers-16-01740" class="html-bibr">29</a>].</p>
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<p>Left: Simplified schematics of directed self-assembly routes. Colors represent polymers with distinct repeat units. Right: (<b>a</b>) Nitroxide-mediated radical polymerization for hydroxyl-terminated end-functionalized RCPs inspired by Mansky’s study. (<b>b</b>) Alternative confinement of a BCP thin-film using RCP derivatives [<a href="#B39-polymers-16-01740" class="html-bibr">39</a>]. Adapted with permission from reference [<a href="#B39-polymers-16-01740" class="html-bibr">39</a>].</p>
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<p>PS and PMMA RCPs of (<b>a</b>) end-hydroxyl functionalized brush, (<b>b</b>) side-chain hydroxyl-containing brush, (<b>c</b>) schematic of (<b>a</b>) and (<b>b</b>), respectively, based on the work of Nealey and Gopalan, followed by an SEM image of BCP of PS-<span class="html-italic">b</span>-PMMA (52-<span class="html-italic">b</span>-52) atop a side-chain brush of f<sub>St</sub> = 0.58, f<sub>MMA</sub> = 0.41, and f<sub>HEMA</sub> = 0.01 [<a href="#B40-polymers-16-01740" class="html-bibr">40</a>]. Adapted with permission from reference [<a href="#B40-polymers-16-01740" class="html-bibr">40</a>].</p>
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<p>Epoxy-containing RCP for use as cross-linking neutral mat with a schematic of achieved neutrality of BCP of PS-<span class="html-italic">b</span>-PMMA (52-<span class="html-italic">b</span>-52) atop the cross-linked neutral mat. f<sub>GMA</sub> = 0.01 for all images and varies by styrene fractions such that: (<b>a</b>) f<sub>St</sub> = 0.48, (<b>b</b>) f<sub>St</sub> = 0.53, (<b>c</b>) f<sub>St</sub> = 0.56, (<b>d</b>) f<sub>St</sub> = 0.59, and (<b>e</b>) f<sub>St</sub> = 0.63, scale bar represents 200 nm [<a href="#B43-polymers-16-01740" class="html-bibr">43</a>]. Adapted with permission from reference [<a href="#B43-polymers-16-01740" class="html-bibr">43</a>].</p>
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<p>(Left) Block cooligomer brushes (1.6–2.5 kg/mol) of f<sub>St</sub> = 0.64 grafted onto the substrate prior to annealing the BCP of PS-<span class="html-italic">b</span>-PMMA (52-<span class="html-italic">b</span>-52) atop. (Right) Nitroxide-mediated polymerization of O(S-<span class="html-italic">b</span>-M<span class="html-italic">r</span>H) block cooligomer [<a href="#B21-polymers-16-01740" class="html-bibr">21</a>]. Adapted with permission from reference [<a href="#B21-polymers-16-01740" class="html-bibr">21</a>].</p>
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<p>Water contact angle measurements of hydroxy-terminated PS (Mn = 3.8 kg/mol) and PMMA (Mn = 4.4 kg/mol) as a function of PS composition with corresponding optical microscopy images of 80 nm thick film with equal weights of PS = 22 kg/mol and PMMA = 23 kg/mol annealed atop PS and PMMA brushes with compositions (<b>a</b>) 100% PMMA-OH, (<b>b</b>) 60% PS, (<b>c</b>) 80% PS, and (<b>d</b>) 100% PS [<a href="#B44-polymers-16-01740" class="html-bibr">44</a>]. Adapted with permission from reference [<a href="#B44-polymers-16-01740" class="html-bibr">44</a>].</p>
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<p>(Left) Water contact angles of PS brushes before modification (grey), after PMMA-OH 20 (kg/mol) insertion (orange), and PS brushes treated with PMMA 20 (20 kg/mol) (teal). (Right) SEM images of BCP PS-<span class="html-italic">b</span>-PMMA (52-<span class="html-italic">b</span>-52) annealed on the inserted brushes of PMMA in PS with the relative Mn as follows: PS:PMMA (kg/mol) (<b>a</b>) 3:20, (<b>b</b>) 6:20, (<b>c</b>) 9:20, and (<b>d</b>) 20:20 [<a href="#B14-polymers-16-01740" class="html-bibr">14</a>]. Adapted with permission from reference [<a href="#B14-polymers-16-01740" class="html-bibr">14</a>].</p>
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<p>(<b>a</b>) SEM images of self-assembled PS-<span class="html-italic">b</span>-PMMA (52k-<span class="html-italic">b</span>-52k) on homopolymer brushes made from a blend solution (1 wt%) containing 70% BCP blender (5k-<span class="html-italic">b</span>-5k) and 30% homopolymers of PS-OH (6 k) and PMMA-OH (6 k) before rinsing. The following images display these ratios of the 30% homopolymer brushes of PS:PMMA: (<b>i</b>) 6:4, (<b>ii</b>) 5:5, and (<b>iii</b>) 4:6 [<a href="#B23-polymers-16-01740" class="html-bibr">23</a>]. (<b>b</b>) SEM images of PS-<span class="html-italic">b</span>-PMMA (50k-<span class="html-italic">b</span>-50k) on long-chain binary homopolymer-blend brushes grafted without a BCP blender using PS-OH (16 kg/mol) and PMMA-OH (15 kg/mol). The following images represent these ratios of the cast blend PS:PMMA: (<b>i</b>) 85:15, (<b>ii</b>) 80:20, and (<b>iii</b>) 75:25 [<a href="#B15-polymers-16-01740" class="html-bibr">15</a>]. Adapted with permission from references [<a href="#B15-polymers-16-01740" class="html-bibr">15</a>,<a href="#B23-polymers-16-01740" class="html-bibr">23</a>].</p>
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<p>(Left): Schematic of two-step insertion process of homopolymers for a neutral surface using PS-OH (17.4 kg/mol) and PDMS-OH (17.8 kg/mol) to orient cylinder-forming BCPs: PS-b-PDMS [<a href="#B45-polymers-16-01740" class="html-bibr">45</a>]. (Right): Tapping mode SPM topographical images of PS-OH (71.6% surface composition) and PDMS-OH (28.4% surface composition) with schematics depicting expected brush and amplitude fluctuations. (Top) is a weak PS-selective solvent, (middle) is a moderately PS-selective solvent, and (bottom) is a highly PS-selective solvent [<a href="#B68-polymers-16-01740" class="html-bibr">68</a>]. Adapted with permission from reference [<a href="#B68-polymers-16-01740" class="html-bibr">68</a>].</p>
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21 pages, 13283 KiB  
Article
Quantitative Analysis of Morphology and Surface Properties of Poly(lactic acid)/Poly(ε-caprolactone)/Hydrophilic Nano-Silica Blends
by Sanja Mahović Poljaček, Dino Priselac, Tamara Tomašegović, Mirela Leskovac, Aleš Šoster and Urška Stanković Elesini
Polymers 2024, 16(12), 1739; https://doi.org/10.3390/polym16121739 - 19 Jun 2024
Viewed by 1213
Abstract
A quantitative analysis of the morphology, as well as an analysis of the distribution of components and surface/interfacial properties in poly(lactic acid)(PLA) InegoTM 3251D, poly(ε-caprolactone) (PCL) Capa 6800 and nano-silica (SiO2) Aerosil®200 blends, was conducted in this research. The [...] Read more.
A quantitative analysis of the morphology, as well as an analysis of the distribution of components and surface/interfacial properties in poly(lactic acid)(PLA) InegoTM 3251D, poly(ε-caprolactone) (PCL) Capa 6800 and nano-silica (SiO2) Aerosil®200 blends, was conducted in this research. The study aimed to improve the understanding of how PLA, PCL, and nano-SiO2 interact, resulting in the specific morphology and surface properties of the blends. Samples were produced by varying the concentration of all three components. They were analyzed using SEM, EDS mapping, water contact angle measurements, surface free energy calculation, adhesion parameter measurements, and FTIR-ATR spectroscopy. The results showed that the addition of SiO2 nanoparticles led to an increase in the contact angle of water, making the surface more hydrophobic. SEM images of the blends showed that increasing the PCL content reduced the size of spherical PCL elements in the blends. FTIR-ATR analysis showed that SiO2 nanoparticles influenced the structure ordering of PLA in the blend with equal portions of PLA and PCL. In the samples with a higher PCL content, the spherical elements present in the samples with a higher PLA/PCL ratio have been reduced, indicating better interactions at the interface between PLA, PCL, and SiO2. SEM-EDS mapping of the PLA/PCL 100/0 blend surfaces revealed the presence of SiO2 clusters and the silicon (Si) concentration reaching up to ten times higher than the nominal concentration of SiO2. However, with the addition of 3% SiO2 to the blend containing PCL, the structure became more granular. Specifically, Si protrusions in the sample PLA/PCL 90/10 with 3% SiO2 displayed 29.25% of Si, and the sample PLA/PCL 70/30 with 3% SiO2 displayed an average of 10.61% of Si at the protrusion locations. The results confirmed the affinity of SiO2 to be encapsulated by PCL. A better understanding of the interactions between the materials in the presented blends and the quantitative analysis of their morphology could improve the understanding of their properties and allow the optimization of their application for different purposes. Full article
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<p>SEM micrographs of fracture surfaces of PLA/PCL/SiO<sub>2</sub> samples: (<b>a</b>) without SiO<sub>2</sub>, (<b>b</b>) with 1% SiO<sub>2</sub>, and (<b>c</b>) with 3% SiO<sub>2</sub> (mag. 3000×). Black arrows show spherical PCL domains, red arrows show agglomerates of nano-SiO<sub>2</sub>, and white arrows mark the cracks and slight delamination of the materials.</p>
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<p>Contact angle of water on PLA/PCL and PLA/PCL/SiO<sub>2</sub> blends.</p>
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<p>Surface free energy of PLA/PCL blends with: (<b>a</b>) 0% SiO<sub>2</sub>, (<b>b</b>) 1% SiO<sub>2</sub>, and (<b>c</b>) 3% SiO<sub>2</sub>.</p>
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<p>FTIR – ATR spectra of PLA/PCL blends with: (<b>a</b>) 0% SiO<sub>2</sub>, (<b>b</b>) 1% SiO<sub>2</sub>, and (<b>c</b>) 3% SiO<sub>2</sub>.</p>
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<p>FTIR – ATR spectra of PLA/PCL blends: (<b>a</b>) PLA/PCL 100/0, (<b>b</b>) PLA/PCL 70/30, and (<b>c</b>) PLA/PCL 50/50.</p>
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<p>The SEM – EDS line-scan profile of sample PLA/PLC/SiO<sub>2</sub> 100/0/1 (light – colored graph represents the raw signal intensity line, whereas the dark – colored graph denotes the averaged intensity line).</p>
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<p>The EDS element distribution map of sample PLA/PCL/SiO<sub>2</sub> 100/0/3 with the Si-rich particles (arrows indicate Si-rich densifications).</p>
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<p>Surface morphology of the sample PLA/PCL 90/10 with added (<b>a</b>) 1% SiO<sub>2</sub> and (<b>b</b>) 3% SiO<sub>2</sub> (mag. 1000×).</p>
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<p>Surface morphology of the sample PLA/PCL 70/30 with added (<b>a</b>) 1% SiO<sub>2</sub> and (<b>b</b>) 3% SiO<sub>2</sub>. The points on the images indicate areas analyzed by the SEM-EDS.</p>
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<p>PLA matrix (lighter areas) and PCL component (darker areas) in the sample PLA/PCL 50/50 with added (<b>a</b>) 1% SiO<sub>2</sub> and (<b>b</b>) 3% SiO<sub>2</sub> (mag. 350×).</p>
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<p>The line − scan profile of the PLA/PCL/SiO<sub>2</sub> 50/50/3 sample (light − colored graph represents the raw signal intensity line, whereas the dark − colored graph denotes the averaged intensity line).</p>
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21 pages, 6224 KiB  
Article
Hybrid Zinc Phthalocyanine/PVDF-HFP System for Reducing Biofouling in Water Desalination: DFT Theoretical and MolDock Investigations
by Bassem Jamoussi, Mohhamed Naif M. Al-Sharif, Lassaad Gzara, Hussam Organji, Talal B. Almeelbi, Radhouane Chakroun, Bandar A. Al-Mur, Naief H. M. Al Makishah, Mohamed H. F. Madkour, Fahed A. Aloufi and Riyadh F. Halawani
Polymers 2024, 16(12), 1738; https://doi.org/10.3390/polym16121738 - 19 Jun 2024
Viewed by 1681
Abstract
Fouling and biofouling remain significant challenges in seawater desalination plants. One practical approach to address these issues is to develop anti-biofouling membranes. Therefore, novel hybrid zinc phthalocyanine/polyvinylidene fluoride-co-hexafluoropropylene (Zn(4-PPOx)4Pc/PVDF-HFP) membranes were prepared by electrospinning to evaluate their properties against biofouling. The [...] Read more.
Fouling and biofouling remain significant challenges in seawater desalination plants. One practical approach to address these issues is to develop anti-biofouling membranes. Therefore, novel hybrid zinc phthalocyanine/polyvinylidene fluoride-co-hexafluoropropylene (Zn(4-PPOx)4Pc/PVDF-HFP) membranes were prepared by electrospinning to evaluate their properties against biofouling. The hybrid nanofiber membrane was characterized by atomic force microscopy (AFM), attenuated total reflectance-Fourier transform infrared (ATR-FTIR) spectroscopy, and contact angle measurements. The theoretical calculations of PVDF-HFP, Zn(4-PPOx)4Pc), and Zn(4-PPOx)4Pc/PVDF-HFP nanofibers were performed using a hybrid functional RB3LYP and the 6-31 G (d,p) basis set, employing Gaussian 09. DFT calculations illustrated that the calculated physical and electronic parameters ensured the feasibility of the interaction of PVDF-HFP with Zn(4-PPOx)4Pc via a halogen–hydrogen bond, resulting in a highly stable and remarkably reactive structure. Moreover, molecular electrostatic potential (MEP) maps were drawn to identify the reactive regions of the Zn(4-PPOx)4Pc and PVDF-HFP/Zn(4-PPOx)4Pc nanofibers. Molecular docking analysis revealed that Zn(4-PPOx)4Pc has highest binding affinity (−8.56 kcal/mol) with protein from S. aureus (1N67) mainly with ten amino acids (ASP405, LYS374, GLU446, ASN406, ALA441, TYR372, LYS371, TYR448, LYS374, and ALA442). These findings highlight the promising potential of Zn(4-PPOx) 4Pc/PVDF-HFP nanocomposite membranes in improving the efficiency of water desalination by reducing biofouling and providing antibacterial properties. Full article
(This article belongs to the Special Issue Advanced Polymer Materials for Water and Wastewater Treatment)
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<p>Syntesis of 4-(4-propylphenoxy) phthalonitrile.</p>
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<p>Synthesis of zinc 2,9,16,23-tetra(4-propylphenoxy) phthalocyanine.</p>
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<p>Membrane manufacturing process by the electrospinning device.</p>
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<p>Crystal structures of bacterial proteins from <span class="html-italic">E. coli</span> (PDB ID: 4XO8) (<b>a</b>), <span class="html-italic">S. aureus</span> (PDB ID: 1N67) (<b>b</b>), and <span class="html-italic">P. aeruginosa</span> (PDB ID:3PBQ) (<b>c</b>).</p>
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<p>UV-Vis Spectrum of Zn(4-PPOx)<sub>4</sub>Pc.</p>
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<p>FTIR results of PVDF-HFP/Zn(4-PPOx)<sub>4</sub>Pc (<b>a</b>) and PVDF-HFP (<b>b</b>) membrane.</p>
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<p>3D configuration of PVDF-HFP/Zn(4-PPOx)<sub>4</sub>Pc (<b>a</b>) and PVDF-HFP (<b>b</b>) membrane with a ratio of 50 µm.</p>
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<p>Contact angle and surface tension of the PVDF-HFP/Zn (4-PPOx)4Pc and PVDF-HFP membranes.</p>
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<p>Cos (angle) and surface tension of PVDF-HFP/Zn (4-PPOx)<sub>4</sub>Pc and PVDF-HFP membranes.</p>
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<p>Model molecules for PVDF-HFP (<b>a</b>), Zn(4-PPOx)<sub>4</sub>Pc (<b>b</b>) and PVDF-HFP/Zn(4-PPOx)<sub>4</sub>Pc (<b>c</b>) calculated at B3LYP/LANL2DZ level. [C in grey, H in white grey, O in red, N in blue, Zn in purple and F in light blue].</p>
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<p>HOMO-LUMO orbital distribution with its bandgap energy (ΔE) for Model molecules for PVDF-HFP (<b>a</b>), Zn(4-PPOx)<sub>4</sub>Pc (<b>b</b>) and PVDF-HFP/Zn(4-PPOx)<sub>4</sub>Pc (<b>c</b>) calculated at B3LYP/6-31G+(d,p) level.</p>
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<p>MESP maps for Zn(4-PPOx)<sub>4</sub>Pc (<b>a</b>), PVDF-HFP (<b>b</b>), and PVDF-HFP/Zn(4-PPOx)<sub>4</sub>Pc (<b>c</b>) calculated at B3LYP/6-31 G(d,p) level.</p>
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<p>Two-dimensional illustration of interactions of (<b>a</b>) <span class="html-italic">E. coli</span> (4XO8)-[PPPcZn]—(<b>b</b>) <span class="html-italic">P. aeruginosa</span> (3PBQ) [PPPcZn]—(<b>c</b>) <span class="html-italic">S. aureus</span> (1N67)-[PPPcZn].</p>
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<p>Molecular docking data of <span class="html-italic">E. coli</span> (4XO8)-[Zn(4-PPOx)<sub>4</sub>Pc] complex; (<b>a</b>) specific interaction of Zn(4-PPOx)<sub>4</sub>Pc; (<b>b</b>) hydrophobic surfaces; (<b>c</b>) aromatic surface, (<b>d</b>) bonding surface of hydrogen, (<b>e</b>) ionizability, and (<b>f</b>) solvent-accessible surface (SAS).</p>
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<p>Molecular docking data of <span class="html-italic">P. aeruginosa</span> (3PBQ)-[Zn(4-PPOx)<sub>4</sub>Pc] complex; (<b>a</b>) Specific interaction of Zn(4-PPOx)<sub>4</sub>Pc, (<b>b</b>) hydrophobic surfaces; (<b>c</b>) aromatic surface, (<b>d</b>) bonding surface of hydrogen, (<b>e</b>) ionizability, and (<b>f</b>) solvent-accessible surface (SAS).</p>
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<p>Molecular docking data of <span class="html-italic">S. aureus</span> (1N67)-[Zn(4-PPOx)<sub>4</sub>Pc]; (<b>a</b>) specific interaction of Zn(4-PPOx)<sub>4</sub>Pc; (<b>b</b>) hydrophobic surfaces; (<b>c</b>) aromatic surface, (<b>d</b>) bonding surface of hydrogen, (<b>e</b>) ionizability, and (<b>f</b>) solvent-accessible surface (SAS).</p>
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2 pages, 617 KiB  
Correction
Correction: Zanchetta et al. Effects of Electrospun Fibrous Membranes of PolyCaprolactone and Chitosan/Poly(Ethylene Oxide) on Mouse Acute Skin Lesions. Polymers 2020, 12, 1580
by Flávia Cristina Zanchetta, Rafael Bergamo Trinca, Juliany Lino Gomes Silva, Jéssica da Silva Cunha Breder, Thiago Anselmo Cantarutti, Sílvio Roberto Consonni, Ângela Maria Moraes, Eliana Pereira de Araújo, Mario José Abdalla Saad, Gary G. Adams and Maria Helena Melo Lima
Polymers 2024, 16(12), 1737; https://doi.org/10.3390/polym16121737 - 19 Jun 2024
Viewed by 2744
Abstract
In the original publication, the authors claimed that Figure 6 reporting Western blot data was erroneous as published [...] Full article
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Figure 6

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<p>Western blot analysis and densitometric analysis of smooth muscle actin (α-SMA), PCNA, Tumor Necrosis Factor (TNF-α), and VEGF observed in the excision lesions of mice topically treated with PCL or PCL+CHI/PEO membrane on days 3, 7, and 14. The results were expressed as mean ± standard deviation. (*) <span class="html-italic">p</span> &lt; 0.05 indicates statistically significant differences between treatments according to the Student’s <span class="html-italic">t</span>-test. (<span class="html-italic">n</span> = 4–6). Protein expression levels were standardized against the internal β-actin expression levels of each sample.</p>
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15 pages, 2880 KiB  
Article
Hydrophilization and Functionalization of Fullerene C60 with Maleic Acid Copolymers by Forming a Non-Covalent Complex
by Nadezhda A. Samoilova, Maria A. Krayukhina, Zinaida S. Klemenkova, Alexander V. Naumkin, Michail I. Buzin, Yaroslav O. Mezhuev, Evgeniy A. Turetsky, Sergey M. Andreev, Nelya M. Anuchina and Dmitry A. Popov
Polymers 2024, 16(12), 1736; https://doi.org/10.3390/polym16121736 - 19 Jun 2024
Viewed by 1589
Abstract
In this study, we report an easy approach for the production of aqueous dispersions of C60 fullerene with good stability. Maleic acid copolymers, poly(styrene-alt-maleic acid) (SM), poly(N-vinyl-2-pyrrolidone-alt-maleic acid) (VM) and poly(ethylene-alt-maleic acid) (EM) were used to [...] Read more.
In this study, we report an easy approach for the production of aqueous dispersions of C60 fullerene with good stability. Maleic acid copolymers, poly(styrene-alt-maleic acid) (SM), poly(N-vinyl-2-pyrrolidone-alt-maleic acid) (VM) and poly(ethylene-alt-maleic acid) (EM) were used to stabilize C60 fullerene molecules in an aqueous environment by forming non-covalent complexes. Polymer conjugates were prepared by mixing a solution of fullerene in N-methylpyrrolidone (NMP) with an aqueous solution of the copolymer, followed by exhaustive dialysis against water. The molar ratios of maleic acid residues in the copolymer and C60 were 5/1 for SM and VM and 10/1 for EM. The volume ratio of NMP and water used was 1:1.2–1.6. Water-soluble complexes (composites) dried lyophilically retained solubility in NMP and water but were practically insoluble in non-polar solvents. The optical and physical properties of the preparations were characterized by UV-Vis spectroscopy, FTIR, DLS, TGA and XPS. The average diameter of the composites in water was 120–200 nm, and the ξ-potential ranged from −16 to −20 mV. The bactericidal properties of the obtained nanostructures were studied. Toxic reagents and time-consuming procedures were not used in the preparation of water-soluble C60 nanocomposites stabilized by the proposed copolymers. Full article
(This article belongs to the Special Issue Polymer-Containing Nanomaterials: Synthesis, Properties, Applications)
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<p>Aqueous solutions and dry forms of polymer–fullerene samples: 1—C<sub>60</sub>/SM, 2—C<sub>60</sub>/EM, 3—C<sub>60</sub>/VM.</p>
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<p>Absorption spectra of water solutions of copolymers and C<sub>60</sub> conjugates: 1—EM, 2—SM, 3—VM; 4—C<sub>60</sub>/SM, 5—C<sub>60</sub>/VM, 6—C<sub>60</sub>/EM; (C = 80–90 μg/mL, l = 0.2 cm); 7—C<sub>60</sub>/VM after drying and dissolving (C = 100 μg/mL).</p>
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<p>FTIR spectra of samples containing copolymers: (<b>a</b>) VM, (<b>b</b>) EM and (<b>c</b>) SM; initial copolymers (<b>a1</b>–<b>c1</b>) and fullerene conjugates (<b>a2</b>–<b>c2</b>).</p>
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<p>FTIR spectra of samples containing copolymers: (<b>a</b>) VM, (<b>b</b>) EM and (<b>c</b>) SM; initial copolymers (<b>a1</b>–<b>c1</b>) and fullerene conjugates (<b>a2</b>–<b>c2</b>).</p>
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<p>TGA curves of samples containing VM (<b>a</b>), EM (<b>b</b>) and SM (<b>c</b>) copolymers: 1—copolymers, 2—mechanical mixtures of copolymer with C<sub>60</sub>, 3—hybrid structures and 4—C<sub>60</sub>. Heating rate of 10 °C/min (argon atmosphere).</p>
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<p>TGA curves: 1—C<sub>60</sub> after dialysis and lyophilic drying, 2—pristine C<sub>60</sub>.</p>
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<p>The high-resolution C 1s spectra normalized by the intensity of the main peak ((<b>a</b>) 1—C<sub>60</sub>/SM, 2—C<sub>60</sub>/EM, 3—C<sub>60</sub>/VM), sample C<sub>60</sub>/SM (<b>b</b>), sample C<sub>60</sub>/EM (<b>c</b>) and sample C<sub>60</sub>/VM (<b>d</b>). Black—experimental line, green—Gaussian profiles used for fitting, red—result of fitting.</p>
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15 pages, 5650 KiB  
Article
Crystallization Behavior and Mechanical Property of Biodegradable Poly(butylene succinate-co-2-methyl succinate)/Cellulose Nanocrystals Composites
by Wenxin Yao, Siyu Pan and Zhaobin Qiu
Polymers 2024, 16(12), 1735; https://doi.org/10.3390/polym16121735 - 19 Jun 2024
Cited by 1 | Viewed by 890
Abstract
Biodegradable poly(butylene succinate-co-2-methyl succinate) (PBSMS)/cellulose nanocrystals (CNC) composites were successfully prepared at low CNC loadings with the aims of improving crystallization and mechanical properties and extending the practical application of PBSMS. CNC is finely dispersed in the PBSMS matrix without obvious [...] Read more.
Biodegradable poly(butylene succinate-co-2-methyl succinate) (PBSMS)/cellulose nanocrystals (CNC) composites were successfully prepared at low CNC loadings with the aims of improving crystallization and mechanical properties and extending the practical application of PBSMS. CNC is finely dispersed in the PBSMS matrix without obvious aggregations. The low content of CNC obviously promoted the crystallization behavior of PBSMS under different conditions. The spherulitic morphology study revealed that CNC, as an effective heterogeneous nucleating agent, provided more nucleation sites during the melt crystallization process. In addition, the nucleation effect of CNC was quantitatively evaluated by the following two parameters, i.e., nucleation activity and nucleation efficiency. The crystal structure and crystallization mechanism of PBSMS remained unchanged in the composites. In addition, as a reinforcing nanofiller, CNC significantly increased Young’s modulus and the yield strength of PBSMS. The crystallization behavior and mechanical properties of PBSMS were significantly improved by the low content of CNC, which should be interesting and essential from the perspective of biodegradable polymer composites. Full article
(This article belongs to the Special Issue Sustainable Bio-Based and Circular Polymers and Composites)
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<p>The standard self-nucleation procedure.</p>
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<p>Fractured surface morphology images of (<b>a</b>) PBSMS, (<b>b</b>) PBSMS/CNC0.5, and (<b>c</b>) PBSMS/CNC1.</p>
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<p>(<b>a</b>) Nonisothermal melt crystallization behavior of PBSMS and its composites at 10 °C/min, (<b>b</b>) nonisothermal melt crystallization behavior of PBSMS/CNC0.5 at different cooling rates, and (<b>c</b>) variation of <span class="html-italic">T</span><sub>cc</sub> with <span class="html-italic">Φ</span> for PBSMS and its composites.</p>
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<p>(<b>a</b>) Nonisothermal melt crystallization behavior of PBSMS and its composites at 10 °C/min, (<b>b</b>) nonisothermal melt crystallization behavior of PBSMS/CNC0.5 at different cooling rates, and (<b>c</b>) variation of <span class="html-italic">T</span><sub>cc</sub> with <span class="html-italic">Φ</span> for PBSMS and its composites.</p>
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<p>Plots of relative crystallinity versus crystallization time for PBSMS/CNC0.5.</p>
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<p>Avrami plots of PBSMS/CNC0.5.</p>
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<p>Variation of <span class="html-italic">t</span><sub>0.5</sub> with <span class="html-italic">T</span><sub>c</sub> for PBSMS and its composites.</p>
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<p>Plots of log <span class="html-italic">Φ</span> versus 10<sup>4</sup>/Δ<span class="html-italic">T</span><sub>p</sub><sup>2</sup> for PBSMS and its composites.</p>
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<p>Self-nucleation of PBSMS: (<b>a</b>) melt crystallization from the indicated <span class="html-italic">T</span><sub>s</sub> and (<b>b</b>) subsequent melting behavior (cooling and heating at 10 °C/min).</p>
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<p>The melting behavior of PBSMS and the point data represent the <span class="html-italic">T</span><sub>cs</sub> at indicated <span class="html-italic">T</span><sub>s</sub> values. (The inserted POM images of PBSMS spherulites were cooled from domain I or II).</p>
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<p>WAXD profiles of PBSMS and its composites.</p>
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<p>Spherulitic morphology of (<b>a</b>) PBSMS, (<b>b</b>) PBSMS/CNC0.5, and (<b>c</b>) PBSMS/CNC1. (the same scalar bar).</p>
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<p>Stress–strain curves of PBSMS and its composites.</p>
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<p>Chemical structures of (<b>a</b>) PBSMS and (<b>b</b>) CNC.</p>
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22 pages, 5195 KiB  
Article
Xanthan–Polyurethane Conjugates: An Efficient Approach for Drug Delivery
by Narcis Anghel, Iuliana Spiridon, Maria-Valentina Dinu, Stelian Vlad and Mihaela Pertea
Polymers 2024, 16(12), 1734; https://doi.org/10.3390/polym16121734 - 19 Jun 2024
Viewed by 1046
Abstract
The antifungal agent, ketoconazole, and the anti-inflammatory drug, piroxicam, were incorporated into matrices of xanthan or oleic acid-esterified xanthan (Xn) and polyurethane (PU), to develop topical drug delivery systems. Compared to matrices without bioactive compounds, which only showed a nominal compressive stress of [...] Read more.
The antifungal agent, ketoconazole, and the anti-inflammatory drug, piroxicam, were incorporated into matrices of xanthan or oleic acid-esterified xanthan (Xn) and polyurethane (PU), to develop topical drug delivery systems. Compared to matrices without bioactive compounds, which only showed a nominal compressive stress of 32.18 kPa (sample xanthan–polyurethane) at a strain of 71.26%, the compressive resilience of the biomaterials increased to nearly 50.04 kPa (sample xanthan–polyurethane–ketoconazole) at a strain of 71.34%. The compressive strength decreased to around 30.67 kPa upon encapsulating a second drug within the xanthan–polyurethane framework (sample xanthan–polyurethane–piroxicam/ketoconazole), while the peak sustainable strain increased to 87.21%. The Weibull model provided the most suitable fit for the drug release kinetics. Unlike the materials based on xanthan–polyurethane, those made with oleic acid-esterified xanthan–polyurethane released the active ingredients more slowly (the release rate constant showed lower values). All the materials demonstrated antimicrobial effectiveness. Furthermore, a higher volume of piroxicam was released from oleic acid-esterified xanthan–polyurethane–piroxicam (64%) as compared to xanthan–polyurethane–piroxicam (44%). Considering these results, materials that include polyurethane and either modified or unmodified xanthan showed promise as topical drug delivery systems for releasing piroxicam and ketoconazole. Full article
(This article belongs to the Special Issue Progress in Polymer Networks)
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<p>FTIR spectra of xanthan (a) and xanthan esterified with oleic acid (b).</p>
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<p><sup>1</sup>H–NMR spectra for Xa (<b>a</b>) and XaAO (<b>b</b>).</p>
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<p>FTIR spectra for materials containing unmodified xanthan: (a) Xn-PU; (b) Xn-PU-P; (c) Xn-PU-K; (d) Xn-PU-P/K.</p>
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<p>FTIR spectra for materials containing xanthan esterified with oleic acid: (a) XnOA-PU; (b) XnOA-PU-P; (c) XnOA-PU-K; (d) XnOA-PU-P/K.</p>
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<p>Mechanical properties of swollen Xn-PU-based formulations under compression: (<b>A</b>) Stress–strain profiles of Xn-PU-based formulations; (<b>B</b>) linear dependence of stress–strain curves; (<b>C</b>) elastic modulus calculated according to the standard procedure; (<b>D</b>) maximum sustained compression (dark blue color) and compressive strength (light blue color). The standard deviation is presented as error bars.</p>
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<p>Mechanical properties of swollen XnOA-PU-based formulations under compression: (<b>A</b>) Stress–strain profiles of XnOA-PU-based formulations; (<b>B</b>) linear dependence of stress–strain curves (<b>C</b>) elastic modulus (dark blue color) calculated according to the standard procedure; (<b>D</b>) maximum sustained compression (dark blue color) and compressive strength (light blue color). The standard deviation is presented as error bars.</p>
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<p>SEM micrographs of biomaterials.</p>
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<p>Cumulative drug release over time for biomaterials containing only one bioactive principle.</p>
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<p>Cumulative drug release over time for biomaterials containing both bioactive principles.</p>
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<p>Drug loading capacity of xanthan–polyurethane matrices for piroxicam, ketoconazole, and a combination of both.</p>
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<p>Drug loading efficiency of xanthan–polyurethane matrices for piroxicam, ketoconazole, and a combination of both.</p>
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<p>In vitro anti-inflammatory activity of the tested materials: (a) Xn-PU; (b) Xn-PU-P; (c) Xn-PU-K; (d) Xn-PU-P/K; (e) XnOA-PU; (f) XnOA-PU-P; (g) XnOA-PU-K; (h) XnOA-PU-P/K.</p>
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<p>Synthesis of xanthan oleate.</p>
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<p>Synthesis pathways of polyurethane water dispersion.</p>
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15 pages, 8343 KiB  
Article
Structural Behavior of High Durability FRP Helical Screw Piles Installed in Reclaimed Saline Land
by Sun-Hee Kim, Hyung-Joong Joo and Wonchang Choi
Polymers 2024, 16(12), 1733; https://doi.org/10.3390/polym16121733 - 19 Jun 2024
Viewed by 1024
Abstract
The bearing capacity of fiber-reinforced plastic (FRP) helical screw piles is determined by the lesser of the breaking load at the bolted joint and the resistance provided by the screw tip area. In this study, compression and tensile tests were performed with the [...] Read more.
The bearing capacity of fiber-reinforced plastic (FRP) helical screw piles is determined by the lesser of the breaking load at the bolted joint and the resistance provided by the screw tip area. In this study, compression and tensile tests were performed with the number of bolts and edge distance as variables. It showed similar strength when compared to the failure stress derived from material testing. In addition, considering load resistance performance, the optimal screw cross section was obtained through parametric analysis. Considering the structural behavior of the screw, a prediction equation was presented to design the screw cross-section as a tapered cross-section using a theoretical method. As a result of comparing the screw cross-section with the finite element analysis results, it was confirmed that the design stress and analysis stress showed an error of 1.1 MPa and were within the allowable stress of 80 MPa. Full article
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<p>FRP helical screw piles.</p>
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<p>Failure modes of bolts: (<b>a</b>) bearing failure; (<b>b</b>) shear-out failure; (<b>c</b>) block-shear failure; (<b>d</b>) net-tension failure; (<b>e</b>) cleavage failure.</p>
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<p>Compressive strength test of FRP body: (<b>a</b>) FRP_S_1; (<b>b</b>) FRP_S_2; (<b>c</b>) FRP_S_3.</p>
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<p>Compressive strength test results of the FRP body: (<b>a</b>) FRP_S_1; (<b>b</b>) FRP_S_2; (<b>c</b>) FRP_S_3.</p>
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<p>Load–displacement relation for FRP cylindrical tubes.</p>
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<p>Tensile test of the FRP.</p>
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<p>Failure modes of tensile test specimens: (<b>a</b>) detail of specimen; (<b>b</b>) failure mode within upper jig; (<b>c</b>) failure mode of FRP-25-4-1; (<b>d</b>) failure mode of tensile test all specimens.</p>
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<p>Finite element analysis: (<b>a</b>) modeling; (<b>b</b>) boundary conditions and load conditions.</p>
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<p>Example of finite element analysis results (specimen FRP-25-4): (<b>a</b>) stress distribution; (<b>b</b>) von Mises stress.</p>
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<p>Experimental results for bolted connection of FRP helical screw pile: (<b>a</b>) load–displacement relation for FRP by edge distance; (<b>b</b>) load–displacement relation for edge distance of 35 mm.</p>
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<p>Relation between failure load and member edge distance of FRP bolted connection specimens.</p>
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<p>Relation between failure load and number of bolts in FRP specimens.</p>
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<p>FRP screw pile: (<b>a</b>) load transfer structure; (<b>b</b>) design of FRP screw piles.</p>
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<p>FRP screw analysis modeling.</p>
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<p>Finite element analysis results of FRP helical screw pile: (<b>a</b>) maximum stress; (<b>b</b>) minimum stress.</p>
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12 pages, 3569 KiB  
Article
Preparation and Evaluation of PVDF-HFP-Based Gel Electrolyte for Ge-Sensitized Thermal Cell
by Yadong Chai and Sachiko Matsushita
Polymers 2024, 16(12), 1732; https://doi.org/10.3390/polym16121732 - 18 Jun 2024
Viewed by 2275
Abstract
The semiconductor-sensitized thermal cell (STC) is a new thermoelectric conversion technology. The development of nonliquid electrolytes is the top priority for the practical application of the STC. In this study, a novel gel polymer electrolyte (PH-based GPE) composed of poly(vinylidenefluoride-co-hexafluoropropylene) (PH), [...] Read more.
The semiconductor-sensitized thermal cell (STC) is a new thermoelectric conversion technology. The development of nonliquid electrolytes is the top priority for the practical application of the STC. In this study, a novel gel polymer electrolyte (PH-based GPE) composed of poly(vinylidenefluoride-co-hexafluoropropylene) (PH), 1-Methyl-2-pyrrolidone (NMP), and Cu ions was synthesized and applied to the STC system. The PH-based GPE synthesized at 45 °C showed higher open-circuit voltage (−0.3 V), short-circuit current density (59 μA cm−2) and diffusion coefficient (7.82 × 10−12 m2 s−1), indicating that a well-balanced structure among the NMP molecules was formed to generate a high-efficiency conduction path of the Cu ions. Moreover, the ion diffusion lengths decreased with decreasing content rates of NMP for the PH-based GPEs, indicating that the NMP plays an important role in the diffusion of Cu ions. Furthermore, the activation energy was calculated to be 107 kJ mol−1, and that was smaller compared to 150 kJ mol−1 for the poly(ethylene glycol)-based liquid electrolyte. These results play an important reference role in the development of electrolytes for STC systems. At the same time, they also provide a new avenue and reference indicator for the synthesis of high-performance and safe GPEs. Full article
(This article belongs to the Special Issue Polymers for Environmental Remediation and Energy Regeneration)
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<p>(<b>a</b>) Illustration of the cell assembly procedure and (<b>b</b>) digital camera image of the assembled cell.</p>
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<p>FT-IR spectra of (PVDF-HFP) PH, NMP, PH-NMP, NMP-Cu, and PH-NMP-Cu.</p>
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<p>(<b>a</b>–<b>g</b>) Digital camera images of the fabricated cells and (<b>h</b>–<b>n</b>) microphotographs of the electrolytes observed from FTO side at different gelation temperatures ((<b>a</b>,<b>h</b>) 30 °C, (<b>b</b>,<b>i</b>) 35 °C, (<b>c</b>,<b>j</b>) 40 °C, (<b>d</b>,<b>k</b>) 45 °C, (<b>e</b>,<b>l</b>) 50 °C, (<b>f</b>,<b>m</b>) 55 °C, and (<b>g</b>,<b>n</b>) 60 °C).</p>
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<p>(<b>a</b>) FT-IR spectra and (<b>b</b>) content rates of NMP for the electrolytes at different gelation temperatures, where <span class="html-italic">A</span><sub>1</sub> is the absorption band due to C=O stretching vibration of NMP and <span class="html-italic">A</span><sub>2</sub> is the absorption band due to CF<sub>2</sub> stretching vibration of PVDF-HFP.</p>
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<p>(<b>a</b>) Cyclic voltammetry and (<b>c</b>) chronoamperometry of the cells measured at different temperatures which are equal to the gelation temperatures. (<b>b</b>) Open−circuit voltages, short−circuit current densities, and (<b>d</b>) discharge times of the cells are obtained from CV and CP measurements.</p>
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13 pages, 2093 KiB  
Article
An Approach to a Silver Conductive Ink for Inkjet Printer Technology
by Svetlana N. Kholuiskaya, Valentina Siracusa, Gulnaz M. Mukhametova, Luybov A. Wasserman, Vladislav V. Kovalenko and Alexey L. Iordanskii
Polymers 2024, 16(12), 1731; https://doi.org/10.3390/polym16121731 - 18 Jun 2024
Cited by 1 | Viewed by 1677
Abstract
Silver-based metal–organic decomposition inks composed of silver salts, complexing agents and volatile solvents are now the subject of much research due to the simplicity and variability of their preparation, their high stability and their relatively low sintering temperature. The use of this type [...] Read more.
Silver-based metal–organic decomposition inks composed of silver salts, complexing agents and volatile solvents are now the subject of much research due to the simplicity and variability of their preparation, their high stability and their relatively low sintering temperature. The use of this type of ink in inkjet printing allows for improved cost-effective and environmentally friendly technology for the production of electrical devices, including flexible electronics. An approach to producing a silver salt-based reactive ink for jet printing has been developed. The test images were printed with an inkjet printer onto polyimide substrates, and two-stage thermal sintering was carried out at temperatures of 60 °C and 100–180 °C. The structure and electrical properties of the obtained conductive lines were investigated. As a result, under optimal conditions an electrically conductive film with low surface resistance of approximately 3 Ω/square can be formed. Full article
(This article belongs to the Special Issue Applications of 3D Printing for Polymers, 3rd Edition)
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<p>UV-VIS spectra for silver-based ink (photo) over time at temperatures of 20 °C, time 0 min–300 min—1 day; 5 °C, time from 1 to 200 days.</p>
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<p>(<b>a</b>) Particle size distribution of silver ink particles, according to the DLS data. The concentration of Ag is 2.6 wt.%. (<b>b</b>) The scattering curve of a silver ink sample with an error bar (red), and the theoretical intensity curve calculated according to Formula (1) (blue). (<b>c</b>) The histogram and distribution function (<span class="html-italic">R</span>,) of silver particles (SAXS). The concentration of Ag is 1.0 wt.%.</p>
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<p>X-ray diffraction patterns from reactive silver ink annealed at 60 °C for one hour in vacuum.</p>
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<p>An optical microscope image of the cured ink surface magnified 6 times.</p>
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<p>SEM images of the sintered ink cross section on a polyimide film. Two-stage sintering at temperatures of 60° and 150 °C.</p>
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16 pages, 6329 KiB  
Article
Investigation of Recycled Expanded Polyamide Beads through Artificial Ageing and Mechanical Recycling as a Proof of Concept for Circular Economy
by Sören Handtke, Lena Brömstrup, Jörg Hain, Fabian Fischer, Tim Ossowski, Sven Hartwig and Klaus Dröder
Polymers 2024, 16(12), 1730; https://doi.org/10.3390/polym16121730 - 18 Jun 2024
Cited by 1 | Viewed by 1238
Abstract
Car manufacturers are currently challenged with increasing the sustainability of their products and production to comply with sustainability requirements and legislation. One way to enhance product sustainability is by reducing the carbon footprint of fossil-based plastic parts. Particle foams are a promising solution [...] Read more.
Car manufacturers are currently challenged with increasing the sustainability of their products and production to comply with sustainability requirements and legislation. One way to enhance product sustainability is by reducing the carbon footprint of fossil-based plastic parts. Particle foams are a promising solution to achieve the goal of using lightweight parts with minimal material input. Ongoing developments involve the use of expanded particle foam beads made from engineering plastics such as polyamide (EPA). To achieve this, a simulated life cycle was carried out on virgin EPA, including mechanical recycling. The virgin material was processed into specimens using a steam-free method. One series was artificially aged to replicate automotive life cycle stresses, while the other series was not. The mechanical recycling and re-foaming of the minipellets were then carried out, resulting in an EPA particle foam with 100% recycled content. Finally, the thermal and chemical material properties were comparatively analysed. The study shows that the recycled EPA beads underwent polymer degradation during the simulated life cycle, as evidenced by their material properties. For instance, the recycled beads showed a more heterogeneous molecular weight distribution (an increase in PDI from two to three), contained carbonyl groups, and exhibited an increase in the degree of crystallization from approximately 24% to 36%. Full article
(This article belongs to the Special Issue Thermoplastic Foams: Processing, Manufacturing, and Characterization)
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<p>Mean molecular weights and PDI of virgin and recycled PA 6 according to Su et al. [<a href="#B25-polymers-16-01730" class="html-bibr">25</a>] (solid symbols) and Lozano-González et al. [<a href="#B26-polymers-16-01730" class="html-bibr">26</a>] (hollow symbols).</p>
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<p>Artificial life cycle with process steps and position of analyses.</p>
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<p>Dimensions of processed EPA specimen.</p>
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<p>Photographs of three stages of polyamide material that were analysed: virgin expanded polyamide (EPA) particle foam beads (<b>left</b>), minipellets of PA after recycling (<b>middle</b>), and recycled EPA particle foam beads (<b>right</b>).</p>
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<p>SEC curves of virgin EPA beads, minipellets, and recycled EPA beads of differentially aged specimens.</p>
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<p>Average molecular weights and PDI of virgin material (_v), minipellets (_MP), and recyclate beads (_R) by SEC.</p>
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<p>A possible mechanism for chain extension during autoclave foaming is depicted in schematic form. (<b>I</b>: Streched polymer chain, <b>II</b>: Middle segment is fully stretched, <b>III</b>: formation of two active chain ends, <b>IV</b>: forming of branched polymer chain).</p>
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<p>ATR-FTIR absorption of virgin EPA and recyclate beads. (<b>a</b>) Whole spectrum; (<b>b</b>) CO<sub>2</sub> absorption bands; (<b>c</b>) carbonyl region.</p>
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<p>DSC curves of virgin material and recyclate beads.</p>
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<p>Degree of crystallisation of virgin material, minipellets, and recyclate beads.</p>
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<p>Relative shrinkage of single virgin and recyclate beads.</p>
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18 pages, 6495 KiB  
Article
Antibacterial Potential and Biocompatibility of Chitosan/Polycaprolactone Nanofibrous Membranes Incorporated with Silver Nanoparticles
by Viktoriia Korniienko, Yevgeniia Husak, Kateryna Diedkova, Yuliia Varava, Vladlens Grebnevs, Oksana Pogorielova, Māris Bērtiņš, Valeriia Korniienko, Baiba Zandersone, Almira Ramanaviciene, Arunas Ramanavicius and Maksym Pogorielov
Polymers 2024, 16(12), 1729; https://doi.org/10.3390/polym16121729 - 18 Jun 2024
Cited by 7 | Viewed by 1710
Abstract
This study addresses the need for enhanced antimicrobial properties of electrospun membranes, either through surface modifications or the incorporation of antimicrobial agents, which are crucial for improved clinical outcomes. In this context, chitosan—a biopolymer lauded for its biocompatibility and extracellular matrix-mimicking properties—emerges as [...] Read more.
This study addresses the need for enhanced antimicrobial properties of electrospun membranes, either through surface modifications or the incorporation of antimicrobial agents, which are crucial for improved clinical outcomes. In this context, chitosan—a biopolymer lauded for its biocompatibility and extracellular matrix-mimicking properties—emerges as an excellent candidate for tissue regeneration. However, fabricating chitosan nanofibers via electrospinning often challenges the preservation of their structural integrity. This research innovatively develops a chitosan/polycaprolactone (CH/PCL) composite nanofibrous membrane by employing a layer-by-layer electrospinning technique, enhanced with silver nanoparticles (AgNPs) synthesized through a wet chemical process. The antibacterial efficacy, adhesive properties, and cytotoxicity of electrospun chitosan membranes were evaluated, while also analyzing their hydrophilicity and nanofibrous structure using SEM. The resulting CH/PCL-AgNPs composite membranes retain a porous framework, achieve balanced hydrophilicity, display commendable biocompatibility, and exert broad-spectrum antibacterial activity against both Gram-negative and Gram-positive bacteria, with their efficacy correlating to the AgNP concentration. Furthermore, our data suggest that the antimicrobial efficiency of these membranes is influenced by the timed release of silver ions during the incubation period. Membranes incorporated starting with AgNPs at a concentration of 50 µg/mL effectively suppressed the growth of both microorganisms during the early stages up to 8 h of incubation. These insights underscore the potential of the developed electrospun composite membranes, with their superior antibacterial qualities, to serve as innovative solutions in the field of tissue engineering. Full article
(This article belongs to the Special Issue Bio-Inspired Polymers: Synthesis, Properties and Applications)
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<p>Scanning electron microscopy images of electrospun membranes after alkali treatment (<b>A</b>) with a frequency of “fiber’s diameter distribution”, (<b>B</b>) “fiber’s orientation map”, and (<b>C</b>) “fiber’s orientation distribution” (<b>D</b>).</p>
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<p>SEM image of membranes loaded with 50 (<b>A</b>), 100 (<b>B</b>), 200 (<b>C</b>), and 400 (<b>D</b>) µg of AgNPs.</p>
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<p>3D reconstruction of surface morphology of electrospun membranes loaded with 50 (<b>A</b>), 100 (<b>B</b>), 200 (<b>C</b>), and 400 (<b>D</b>) µg of AgNPs. In the insertions—the roughness reconstruction of the membrane texture (Ra, µm; and Rz, µm). In the centrum—values of the static contact angle measurements.</p>
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<p>SEM image and EDX analysis of membranes loaded with 50 (<b>A</b>) (spot analysis), 100 (<b>B</b>), 200 (<b>C</b>), and 400 (<b>D</b>) µg (region analysis) of AgNPs.</p>
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<p>Scanning electron microscopy images of membranes’ cross-section with cross-sectional EDX line scan (violet diagrams) and EDS atomic % of Ag. Figure demonstrating membranes loaded with 50 (<b>A</b>), 100 (<b>B</b>), 200 (<b>C</b>), and 400 (<b>D</b>) µg of AgNPs.</p>
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<p>(<b>A</b>) FTIR spectra of the control sample and sample with the addition of 400 mg·L<sup>−1</sup> of Ag, showing the most characteristic band positions with the accuracy ± 5 cm<sup>−1</sup> in the wavelength range between 3100 and 600 cm<sup>−1</sup>; (<b>B</b>) FTIR spectra of all samples in the wavelength range between 1800 and 1600 cm<sup>−1</sup>.</p>
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<p>Comparison of the Ag ions release levels of CH/PCL-AgNPs membranes at each time point of the experiment.</p>
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<p>Resazurin reduction assay data on the proliferation of human keratinocytes during the 7-day experiment on different CH/PCL-AgNPs membranes (control—CH/PCL; numbers on samples mean amount of AgNPs µg/mL loaded to CH/PCL); <span class="html-italic">p</span>-value less than 0.001 flagged with three stars.</p>
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<p>Disk-diffusion assay: zone of growth inhibition after <span class="html-italic">S. aureus</span> and <span class="html-italic">E. coli</span> (<b>A</b>) and (<b>B</b>) incubation with the electrospun membranes (CH/PCL control (1), CH/PCL—12.5 µg/mL (2), CH/PCL—25 µg/mL (3), CH/PCL—50 µg/mL (4), CH/PCL—100 µg/mL, (5) CH/PCL—200 µg/mL, (6) and (7) CH/PCL—400 µg/mL (7) AgNPs). Positive control was a disk with Ceftazidime (CAZ).</p>
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<p>Evaluation of the antibacterial properties of CH/PCL-AgNPs membranes against <span class="html-italic">S. aureus</span> and <span class="html-italic">E. coli</span> (control—CH/PCL membrane; the amount of AgNPs loaded to CH/PCL represented in µg/mL); *—denotes significant differences between groups and control at *—<span class="html-italic">p</span> ≤ 0.05; **—<span class="html-italic">p</span> ≤ 0.01.</p>
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<p>The count of living bacterial cells attached to the sample surfaces varied across different time intervals during the co-cultivation with <span class="html-italic">E. coli</span> and <span class="html-italic">S. aureus</span> (control—CH/PCL membrane; the amount of AgNPs µg/mL loaded to CH/PCL indicated on the horizontal axis); **—denotes significant differences between groups and control at **—<span class="html-italic">p</span> ≤ 0.01; ***—<span class="html-italic">p</span> ≤ 0.001.</p>
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<p>SEM images of the evaluation of the antibacterial properties of CH/PCL-AgNPs membranes against <span class="html-italic">S. aureus</span> loaded with 200 (<b>A</b>) and 25 (<b>B</b>) µg of AgNPs and <span class="html-italic">E. coli</span> loaded with 200 (<b>C</b>) and 25 (<b>D</b>) µg of AgNPs (presented the most representative SEM images).</p>
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10 pages, 1098 KiB  
Article
Piezoelectric Outputs of Electrospun PVDF Web as Full-Textile Sensor at Different Mechanical Excitation Frequencies
by Fenye Meng and Jiyong Hu
Polymers 2024, 16(12), 1728; https://doi.org/10.3390/polym16121728 - 18 Jun 2024
Viewed by 1031
Abstract
With the increasing application of electrospun PVDF webs in piezoelectric sensors and energy-harvesting devices, it is crucial to understand their responses under complex mechanical excitations. However, the dependence of the piezoelectric effect on mechanical excitation properties is not fully comprehended. This study aims [...] Read more.
With the increasing application of electrospun PVDF webs in piezoelectric sensors and energy-harvesting devices, it is crucial to understand their responses under complex mechanical excitations. However, the dependence of the piezoelectric effect on mechanical excitation properties is not fully comprehended. This study aims to investigate the piezoelectric output of randomly oriented electrospun PVDF nanofiber webs fabricated through different electrospinning processes at various mechanical excitation frequencies. The electrospun PVDF web was sandwiched between two textile electrodes, and its piezoelectric output as a full-textile sensor was measured across a frequency range from 0.1 Hz to 10 Hz. The experimental results revealed that the piezoelectric output of the electrospun PVDF web exhibited a nearly linear increase at excitation frequencies below 1.0 Hz and then reached an almost constant value thereafter up to 10 Hz, which is different from the hybrid PVDF or its copolymer web. Furthermore, the dependency of the piezoelectric output on the excitation frequency was found to be influenced by the specific electrospinning process employed, which determined the crystalline structure of electrospun PVDF nanofibers. These findings suggest that determining an appropriate working frequency for randomly oriented electrospun PVDF nanofiber webs is essential before practical implementation, and the piezoelectric response mode in different mechanical activation frequency ranges can be used to detect different human physiological behaviors. Full article
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<p>(<b>a</b>) A schematic representation of the full-textile pressure sensor and (<b>b</b>) a schematic diagram of the self-made experimental setup for piezoelectric characterization.</p>
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<p>The real-time force and piezoelectric output of the packaged full-textile sensor prototype at different mechanical excitation frequencies: (<b>a</b>) 0.3 Hz; (<b>b</b>) 1.0 Hz. The sensitive material of the sensor prototype was obtained at an applied voltage of 20 kV; (<b>c</b>) the time-dependent activation force; (<b>d</b>) the piezoelectric output under the dynamic activation force.</p>
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<p>The dependence of piezoelectric output on the mechanical excitation frequency. The full-textile sensor prototype is the same as that in <a href="#polymers-16-01728-f002" class="html-fig">Figure 2</a>.</p>
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<p>The effect of the excitation frequency on the output of PVDF nanofiber webs under different electrospinning conditions as full-textile sensors. (<b>a</b>) applied voltage; (<b>b</b>) feeding flow rates; (<b>c</b>) needle-tip diameter.</p>
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19 pages, 9277 KiB  
Article
Bioactivity and Antibacterial Analysis of Plasticized PLA Electrospun Fibers Reinforced with MgO and Mg(OH)2 Nanoparticles
by Adrián Leonés, Valentina Salaris, Laura Peponi, Marcela Lieblich, Alexandra Muñoz-Bonilla, Marta Fernández-García and Daniel López
Polymers 2024, 16(12), 1727; https://doi.org/10.3390/polym16121727 - 18 Jun 2024
Cited by 3 | Viewed by 1305
Abstract
In this work, we focused on the bioactivity and antibacterial behavior of PLA-based electrospun fibers, efibers, reinforced with both MgO and Mg(OH)2 nanoparticles, NPs. The evolution of PLA-based efibers was followed in terms of morphology, FTIR, XRD, and visual appearance. The bioactivity [...] Read more.
In this work, we focused on the bioactivity and antibacterial behavior of PLA-based electrospun fibers, efibers, reinforced with both MgO and Mg(OH)2 nanoparticles, NPs. The evolution of PLA-based efibers was followed in terms of morphology, FTIR, XRD, and visual appearance. The bioactivity was discussed in terms of hydroxyapatite growth after 28 days, considered as T28, of immersion in simulated body fluid, SBF. In particular, the biomineralization process evidenced after immersion in SBF started at T14 in both systems. The number of precipitated crystals increased by increasing the amount of both NPs. The chemical composition of the precipitated crystals was also characterized in terms of the Ca/P molar ratio after T28 of immersion in SBF, indicating the presence of hydroxyapatite on the surface of both reinforced efibers. Moreover, a reduction in the average diameter of the PLA-based efibers was observed, reaching a maximum reduction of 46 and 60% in the average diameter of neat PLA and PLA:OLA efibers, respectively, after 28 days of immersion in SBF. The antibacterial behavior of the MgO and Mg(OH)2 NPs in the PLA-based electrospun fibers was tested against Escherichia coli, E. coli, as the Gram-negative bacteria, and Staphylococcus aureus, S. aureus, as the Gram-positive bacteria, obtaining the best antibacterial activity against the Gram-negative bacteria E. coli of 21 ± 2% and 34 ± 6% for the highest concentration of MgO and Mg(OH)2 NPs, respectively. Full article
(This article belongs to the Special Issue Organic-Inorganic Hybrid Materials III)
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<p>SEM images of PLA and PLA:OLA efibers in SBF at T0, T14, and T28.</p>
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<p>SEM images of PLA:OLA-MgO efibers in SBF at T0, T14, and T28.</p>
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<p>SEM images of PLA:OLA-Mg(OH)<sub>2</sub> efibers in SBF at T0, T14 and T28.</p>
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<p>Diameter size distributions at T0 for the different electrospun fibers studied.</p>
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<p>Average diameter evolution of PLA-based efibers in SBF at T0, T14, and T28 of (<b>a</b>) PLA:OLA-MgO and (<b>b</b>) PLA:OLA-Mg(OH)<sub>2</sub> efibers.</p>
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<p>XRD patterns of (<b>a</b>) PLA and PLA:OLA, (<b>b</b>) PLA:OLA-MgO, and (<b>c</b>) PLA:OLA-Mg(OH)<sub>2</sub> efibers in SBF at T0 (<b>left</b>) and T28 (<b>right</b>).</p>
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<p>FTIR spectra of (<b>a</b>) PLA:OLA-MgO and (<b>b</b>) PLA:OLA-Mg(OH)<sub>2</sub> efibers after immersion in SBF at T0 and T28. Spectra of PLA and PLA:OLA are also included in the graphs.</p>
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<p>FTIR spectra 1800–400 cm<sup>−1</sup> of (<b>a</b>) PLA:OLA-MgO and (<b>b</b>) PLA:OLA-Mg(OH)<sub>2</sub> efibers after immersion in SBF at T28. Spectra of PLA and PLA:OLA are also included in the graphs.</p>
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<p>Images of the control plate and the plasticized PLA electrospun fiber at the highest concentrations of MgO and Mg(OH)<sub>2</sub> NPs against (<b>a</b>) <span class="html-italic">E. coli</span> and (<b>b</b>) <span class="html-italic">S. aureus</span>.</p>
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