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Polymers, Volume 16, Issue 1 (January-1 2024) – 165 articles

Cover Story (view full-size image): Replacing petroleum-based polymers with biopolymers such as polysaccharides is essential for protecting our environment by saving fossil resources. A research field that can benefit from the application of more environmentally friendly and renewable materials is photochemistry. Therefore, cellulose-based photoresists that could be photocrosslinked via UV irradiation were developed. The olefinic cellulose derivatives are based on cellulose diacetate and tosyl cellulose. These biogenic polymers enable the manufacturing of sustainable coatings, even with imprinted microstructures, and cellulose-based bulk materials. Further, the manufactured cellulose-based architectures, even the bulk structures, could be entirely regenerated into pure cellulose devices via a sodium methoxide treatment. View this paper
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27 pages, 5154 KiB  
Review
Surface Modification Progress for PLGA-Based Cell Scaffolds
by Bohua Yan, Yabing Hua, Jinyue Wang, Tianjiao Shao, Shan Wang, Xiang Gao and Jing Gao
Polymers 2024, 16(1), 165; https://doi.org/10.3390/polym16010165 - 4 Jan 2024
Cited by 2 | Viewed by 2933
Abstract
Poly(lactic-glycolic acid) (PLGA) is a biocompatible bio-scaffold material, but its own hydrophobic and electrically neutral surface limits its application as a cell scaffold. Polymer materials, mimics ECM materials, and organic material have often been used as coating materials for PLGA cell scaffolds to [...] Read more.
Poly(lactic-glycolic acid) (PLGA) is a biocompatible bio-scaffold material, but its own hydrophobic and electrically neutral surface limits its application as a cell scaffold. Polymer materials, mimics ECM materials, and organic material have often been used as coating materials for PLGA cell scaffolds to improve the poor cell adhesion of PLGA and enhance tissue adaptation. These coating materials can be modified on the PLGA surface via simple physical or chemical methods, and coating multiple materials can simultaneously confer different functions to the PLGA scaffold; not only does this ensure stronger cell adhesion but it also modulates cell behavior and function. This approach to coating could facilitate the production of more PLGA-based cell scaffolds. This review focuses on the PLGA surface-modified materials, methods, and applications, and will provide guidance for PLGA surface modification. Full article
(This article belongs to the Special Issue Biomedical Applications of Polymeric Materials II)
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<p>Schematic diagram of the ultrasonic coating setup and ultrasonic cavitation near the film surface during the process. Reprinted with permission from Ref. [<a href="#B39-polymers-16-00165" class="html-bibr">39</a>]. Copyright 2023, copyright Springer Nature, London, UK.</p>
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<p>Preparing sintered PLGA microspheres and depositing electrospun nanofibers. The red is cationic chitosan and the blue is anionic HA. Reprinted with permission from Ref. [<a href="#B42-polymers-16-00165" class="html-bibr">42</a>]. Copyright 2023, copyright American Chemical Society, Washington, DC, USA.</p>
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<p>Formation of PDA: A copolymer of 5, 6-dihydroxy indole (DHI) and dopamine. Reprinted with permission from Ref. [<a href="#B83-polymers-16-00165" class="html-bibr">83</a>]. Copyright 2023, copyright John Wiley and Sons, Hoboken, NJ, USA.</p>
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<p>Porous PLGA microspheres coated with PDA so that they may act as a carrier for exosomes. Reprinted with permission from Ref. [<a href="#B3-polymers-16-00165" class="html-bibr">3</a>]. Copyright 2023, copyright Elsevier, Amsterdam, The Netherlands.</p>
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<p>Michael addition and Schiff base reactions of reactive aminating and sulfurylating ligands. Reprinted with permission from Ref. [<a href="#B91-polymers-16-00165" class="html-bibr">91</a>]. Copyright 2023, copyright Frontiers, Lausanne, Switzerland.</p>
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<p>Schematic representation of different cell responses when induced by PLL, PDL, LL9, and DL9. Reprinted with permission from Ref. [<a href="#B9-polymers-16-00165" class="html-bibr">9</a>]. Copyright 2023, copyright America Chemical Society, Washington, DC, USA.</p>
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<p>Ppy-coated PLGA grids. (<b>a</b>) Photos of uncoated PLGA grids (white, left) and Ppy-PLGA grids (black, right); (<b>b</b>) SEM micrograph of a single strand of Ppy-PLGA fibers. (<b>c</b>) SEM image of section of the PPy-PLGA meshes. Reprinted with permission from Ref. [<a href="#B38-polymers-16-00165" class="html-bibr">38</a>]. Copyright 2023, copyright Elsevier, Amsterdam, The Netherlands.</p>
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<p>Synthesis scheme of a cyanide-functional pyrrole (<b>1</b>), a carboxy-functional pyrrole (<b>2</b>), a carboxy-functional Poly(1-(2-carboxyethyl)pyrrole (PpyCOOH) (<b>3</b>), chemically coupled with RGD peptide, RGD grafting PpyCOOH (<b>4</b>). Reprinted with permission from Ref. [<a href="#B116-polymers-16-00165" class="html-bibr">116</a>]. Copyright 2023, copyright American Chemical Society, Washington, DC, USA.</p>
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<p>Structure of Ppy with the dopant (anion) A<sup>−</sup>. Reprinted/adapted with permission from Ref. [<a href="#B103-polymers-16-00165" class="html-bibr">103</a>]. Copyright 2023, copyright Elsevier, Amsterdam, The Netherlands.</p>
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<p>PLGA + gelatin/ALD/NG stent implantation to repair a cranial defect in rats. Reprinted/adapted with permission from Ref. [<a href="#B124-polymers-16-00165" class="html-bibr">124</a>]. Copyright 2023, copyright America Chemical Society, Washington, DC, USA.</p>
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<p>Preparing the PLGA-ECM scaffold. Reprinted/adapted with permission from Ref. [<a href="#B131-polymers-16-00165" class="html-bibr">131</a>]. Copyright 2023, copyright Elsevier, Amsterdam, The Netherlands.</p>
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<p>Adhesive-coated PLGA (LC-YE- PLGA) NGC (YE NGC: Yarn-wrapped neural guiding catheter; LC-YE NGC: Laminin-coated yarn-coated neural guiding catheter). Reprinted/adapted with permission from Ref. [<a href="#B49-polymers-16-00165" class="html-bibr">49</a>]. Copyright 2023, copyright Royal Society of Chemistry, London, UK.</p>
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<p>Diabetic wound repair via the LPS/IFN-γ activation of mouse RAW264.7 cell membranes. Reprinted/adapted with permission from Ref. [<a href="#B142-polymers-16-00165" class="html-bibr">142</a>]. Copyright 2023, copyright Springer Nature, London, UK.</p>
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16 pages, 1847 KiB  
Article
Integral Valorization of Posidonia oceanica Balls: An Abundant and Potential Biomass
by Rim Mnafki, Amaia Morales, Leyre Sillero, Ramzi Khiari, Younes Moussaoui and Jalel Labidi
Polymers 2024, 16(1), 164; https://doi.org/10.3390/polym16010164 - 4 Jan 2024
Viewed by 1462
Abstract
Posidonia oceanica balls (POB), a kind of seagrass, are a significant environmental issue since they are annually discharged onto beaches. Their current usefulness limits interest in their management and enhances the environmental problem. Therefore, in this research, the potential of this lignocellulosic biomass [...] Read more.
Posidonia oceanica balls (POB), a kind of seagrass, are a significant environmental issue since they are annually discharged onto beaches. Their current usefulness limits interest in their management and enhances the environmental problem. Therefore, in this research, the potential of this lignocellulosic biomass was studied from a holistic biorefinery point of view. To this end, an in-depth study was carried out to select the best pathway for the integral valorization of POBs. First, an autohydrolysis process was studied for the recovery of oligosaccharides. Then, a delignification stage was applied, where, in addition to studying different delignification methods, the influence of the autohydrolysis pre-treatment was also investigated. Finally, cellulose nanofibers (CNFs) were obtained through a chemo-mechanical treatment. The results showed that autohydrolysis not only improved the delignification process and its products, but also allowed the hemicelluloses to be valorized. Acetoformosolv delignification proved to be the most successful in terms of lignin and cellulose properties. However, alkaline delignification was able to extract the highest amount of lignin with low purity. CNFs were also successfully produced from bleached solids. Therefore, the potential of POB as a feedstock for a biorefinery was confirmed, and the pathway should be chosen according to the requirements of the desired end products. Full article
(This article belongs to the Special Issue Biopolymers from Renewable Sources)
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<p>FTIR spectra of the raw material, autohydrolyzed solid and delignified solids.</p>
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<p>ATR-FTIR spectra of the obtained three lignins.</p>
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<p>FTIR spectra of the bleached solids and the obtained CNF from bleached solids.</p>
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<p>XRD diffractograms of different CNFs.</p>
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<p>AFM images of (<b>a</b>) CNF-AFW and (<b>b</b>) CNF-A180-AFW.</p>
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31 pages, 4237 KiB  
Review
Anthocyanin-Loaded Polymers as Promising Nature-Based, Responsive, and Bioactive Materials
by S.S. Rosales-Murillo, Julia Sánchez-Bodón, S.L. Hernández Olmos, M.F. Ibarra-Vázquez, L.G. Guerrero-Ramírez, L. Pérez-Álvarez and J.L. Vilas-Vilela
Polymers 2024, 16(1), 163; https://doi.org/10.3390/polym16010163 - 4 Jan 2024
Cited by 5 | Viewed by 2922
Abstract
Anthocyanins are a specific group of molecules found in nature that have recently received increasing attention due to their interesting biological and colorimetric properties that have been successfully applied in several fields such as food preservation and biomedicine. Consequently, reviews devoted to a [...] Read more.
Anthocyanins are a specific group of molecules found in nature that have recently received increasing attention due to their interesting biological and colorimetric properties that have been successfully applied in several fields such as food preservation and biomedicine. Consequently, reviews devoted to a general overview of these flavonoids have proliferated in recent years. Meanwhile, the incorporation of anthocyanins into polymeric systems has become an interesting strategy to widen the applicability of these molecules and develop new smart and functional polymers in the above cited areas. However, anthocyanin-based polymers have been scarcely reviewed in the literature. Accordingly, this review aims to be a systematic summary of the most recent approaches for the incorporation of anthocyanins into macro-, micro-, or nanostructured polymers. Moreover, this work describes the fundamentals of the applicability of smart anthocyanin-based polymers and offers an updated review of their most interesting applications as sensors, biological regulators, and active materials. Full article
(This article belongs to the Section Polymer Applications)
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Graphical abstract

Graphical abstract
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<p>(<b>a</b>) Flavylium ion structure; (<b>b</b>) common numbering of flavylium ion.</p>
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<p>pH-dependent structural changes and color variation of anthocyanins in aqueous solution. Reprinted with permission from Calogero et al. [<a href="#B8-polymers-16-00163" class="html-bibr">8</a>]. Copyright (Calogero G) (Chem Soc Rev).</p>
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<p>Chemical structures of anthocyanin at different pH values. Source: [<a href="#B25-polymers-16-00163" class="html-bibr">25</a>].</p>
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<p>Illustrative scheme of the synthesis and performance of the smart anthocyanin-loaded chitosan/gelatin films for accurate beef sub-freshness monitoring. Reproduced with permission from Li et al. [<a href="#B30-polymers-16-00163" class="html-bibr">30</a>]. Copyright (2024), Elsevier.</p>
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<p>Three-dimensional printing of stable anthocyanin-loaded double emulsion gels formed by pectin and glucono-delta-lactone complexes. Reproduced with permission from Li et al. [<a href="#B51-polymers-16-00163" class="html-bibr">51</a>]. Copyright (2023), Elsevier.</p>
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<p>Triple role of anthocyanin-loaded polymers in food applications.</p>
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<p>Changes in shrimp freshness during storage using intelligent halochromic films. (Reproduced with permission from Tavassoli et al. [<a href="#B113-polymers-16-00163" class="html-bibr">113</a>]). Copyright (2023), Elsevier.</p>
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<p>Changes in the freshness of lamb meat during storage using halochromic smart films. Reproduced with permission from Alizadeh-Sani et al. [<a href="#B116-polymers-16-00163" class="html-bibr">116</a>]. Copyright (2021), Elsevier.</p>
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<p>Changes in the freshness of peeled shrimps (<b>a</b>), rainbow trout fillets (<b>b</b>), minced lamb meat (<b>c</b>), and chicken fillets (<b>d</b>) under cooled conditions using CMC-PLA-VOE 5% after 0 (<b>a</b>), 3 (<b>b</b>), and 7 (<b>c</b>) days. Reproduced with permission from Fatemeh Rezaei et al. [<a href="#B117-polymers-16-00163" class="html-bibr">117</a>]. Copyright (2023), Elsevier.</p>
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<p>Preparation of the anthocyanin-loaded pH-sensing soft contact. (<b>a</b>) Anthocyanin chemical formulas at physiological pH levels: (i) pH 6.5, (ii) pH 7.0, and (iii) pH 7.5. Scale bars: 5.0 mm. (<b>b</b>) Illustration of the different preparation methods: (i) soaking and (ii,iii) drop-casting on the convex/concave face of the contact lenses. (<b>c</b>) Color changes in contact lenses according to the preparation method. Scale bars: 5.0 mm. (<b>d</b>) Micrographs of the cross sections of loaded contact lenses at the different pHs: (i) pH 6.5, (ii) pH 7.0, and (iii) pH 7.5. Scale bars: 200 μm. Reproduced with permission from Riaz et al. [<a href="#B131-polymers-16-00163" class="html-bibr">131</a>]. Copyright (2019) CC, ACS Publications.</p>
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<p>Nanoencapsulates of anthocyanin-enriched extract formed by lipid assembly generated by Mendes et al. [<a href="#B148-polymers-16-00163" class="html-bibr">148</a>] showed successful cellular uptake and improved mitochondrial functionality. Reproduced with the permission of Mendes et al. [<a href="#B148-polymers-16-00163" class="html-bibr">148</a>], licensed under CC BY-NC-ND 4.0 DEED. Copyright (2021), Elsevier.</p>
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18 pages, 4814 KiB  
Article
Protein-Aided Synthesis of Copper-Integrated Polyaniline Nanocomposite Encapsulated with Reduced Graphene Oxide for Highly Sensitive Electrochemical Detection of Dimetridazole in Real Samples
by Kartik Behera, Bhuvanenthiran Mutharani, Yen-Hsiang Chang, Monika Kumari and Fang-Chyou Chiu
Polymers 2024, 16(1), 162; https://doi.org/10.3390/polym16010162 - 4 Jan 2024
Cited by 4 | Viewed by 1447
Abstract
Dimetridazole (DMZ) is a derivative of nitroimidazole and is a veterinary drug used as an antibiotic to treat bacterial or protozoal infections in poultry. The residues of DMZ cause harmful side effects in human beings. Thus, we have constructed a superior electrocatalyst for [...] Read more.
Dimetridazole (DMZ) is a derivative of nitroimidazole and is a veterinary drug used as an antibiotic to treat bacterial or protozoal infections in poultry. The residues of DMZ cause harmful side effects in human beings. Thus, we have constructed a superior electrocatalyst for DMZ detection. A copper (Cu)-integrated poly(aniline) (PANI) electrocatalyst (PANI-Cu@BSA) was prepared by using a one-step method of biomimetic mineralization and polymerization using bovine serum albumin (BSA) as a stabilizer. Then, the synthesized PANI-Cu@BSA was encapsulated with reduced graphene oxide (rGO) using an ultrasonication method. The PANI-Cu@BSA/rGO nanocomposite had superior water dispersibility, high electrical conductivity, and nanoscale particles. Moreover, a PANI-Cu@BSA/rGO nanocomposite-modified, screen-printed carbon electrode was used for the sensitive electrochemical detection of DMZ. In phosphate buffer solution, the PANI-Cu@BSA/rGO/SPCE displayed a current intensity greater than PANI-Cu@BSA/SPCE, rGO/SPCE, and bare SPCE. This is because PANI-Cu@BSA combined with rGO increases fast electron transfer between the electrode and analyte, and this synergy results in analyte–electrode junctions with extraordinary conductivity and active surface areas. PANI-Cu@BSA/rGO/SPCE had a low detection limit, a high sensitivity, and a linear range of 1.78 nM, 5.96 μA μM−1 cm−2, and 0.79 to 2057 μM, respectively. The selective examination of DMZ was achieved with interfering molecules, and the PANI-Cu@BSA/rGO/SPCE showed excellent selectivity, stability, repeatability, and practicability. Full article
(This article belongs to the Special Issue Functional Hybrid Polymeric Composites)
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<p>(<b>a</b>) FE-SEM image of PANI-Cu@BSA and TEM images of (<b>b</b>) PANI-Cu@BSA and (<b>c</b>,<b>d</b>) PANI-Cu@BSA/rGO.</p>
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<p>(<b>a</b>) FTIR spectra of BSA and PANI-Cu@BSA, (<b>b</b>) zeta of PANI-Cu@BSA and PANI-Cu@BSA/rGO, (<b>c</b>) UV spectra of BSA and PANI-Cu@BSA, and (<b>d</b>) Raman spectra of rGO and PANI-Cu@BSA/rGO.</p>
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<p>Core-level XPS spectrum of (<b>a</b>) C 1s, (<b>b</b>) O 1s, (<b>c</b>) N 1s, and (<b>d</b>) Cu 2p for PANI-Cu@BSA/rGO.</p>
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<p>(<b>a</b>) CV profile of the bare SPCE, PANI-Cu@BSA/SPCE, rGO/SPCE, and PANI-Cu@BSA/rGO/SPCE; (<b>b</b>) CV profile of PANI-Cu@BSA/rGO/SPCE at various scan rates (10–100 mV/s) in 5 mM [Fe(CN)<sub>6</sub>]<sup>3−/4−</sup>/0.5 M KCl solution; (<b>c</b>) linear plot of current (I<sub>pa</sub> and I<sub>pc</sub>) vs. (v (mV/s))<sup>1/2</sup>; (<b>d</b>) CV profile of the electrodes including bare, PANI-Cu@BSA, rGO, and PANI-Cu@BSA/rGO modified SPCEs in 150 µM DMZ containing 0.1 M PBS (pH 7) at 50 mV/s.</p>
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<p>(<b>a</b>) CV profile of PANI-Cu@BSA/rGO/SPCE in different concentrations of DMZ (50–250 µM) at 50 mV/s, (<b>b</b>) linear plot of current vs. concentration of DMZ, (<b>c</b>,<b>d</b>) CV profile of the effect of loading level of PANI-Cu@BSA/rGO on the SPCE surface for the detection of DMZ at 50 mV/s, and (<b>d</b>) calibration plot of current vs. loading amount (µL).</p>
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<p>(<b>a</b>) CV profile of PANI-Cu@BSA/rGO/SPCE in various pH ranges from 3 to 11 at 50 mV/s, (<b>b</b>) linear plot of current vs. pH, (<b>c</b>) linear plot of potential vs. pH values, (<b>d</b>) CV profile of PANI-Cu@BSA/rGO/SPCE at various scan rates (0.1 M PBS) from 20 to 120 mV/s, and (<b>e</b>) linear relationship between current and scan rate.</p>
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<p>(<b>a</b>) LSV profile of PANI-Cu@BSA/rGO/SPCE at different concentrations of DMZ from 0.79 to 2057 µM at 50 mV/s, (<b>b</b>) calibration plot of DMZ vs. cathodic peak current (μA) (<span class="html-italic">n</span> = 3), (<b>c</b>) LSV profile of PANI-Cu@BSA/rGO/SPCE on the inferring effect of DMZ with various co-interfering compounds (AZP, CRD, DEX, IRT, LPN, Mg<sup>2+</sup>, Zn<sup>2+</sup>, and NFZ) at 50 mV/s, and (<b>d</b>) corresponding plot of current vs. interfering compounds.</p>
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<p>Pictorial representation of the synthesis process of the PANI-Cu@BSA/rGO.</p>
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<p>(<b>a</b>) Schematic illustration of possible interaction between the DMZ and PANI-Cu@BSA/rGO and (<b>b</b>) the plausible electroreduction mechanism of DMZ on the PANI-Cu@BSA/rGO/SPCE.</p>
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17 pages, 12179 KiB  
Article
Pyrolytic Modification of Heavy Coal Tar by Multi-Polymer Blending: Preparation of Ordered Carbonaceous Mesophase
by Lei Zhang, Chunjiang Liu, Yang Jia, Yidan Mu, Yao Yan and Pengcheng Huang
Polymers 2024, 16(1), 161; https://doi.org/10.3390/polym16010161 - 4 Jan 2024
Cited by 13 | Viewed by 1516
Abstract
In order to achieve the high-value utilization of heavy tar for the production of enhanced-performance graphite foam carbon, the carbon mesophase was ready from the heavy component of low-temperature coal tar, and the coal tar was modified by styrene-butadiene-styrene (SBS), polyethylene (PE) and [...] Read more.
In order to achieve the high-value utilization of heavy tar for the production of enhanced-performance graphite foam carbon, the carbon mesophase was ready from the heavy component of low-temperature coal tar, and the coal tar was modified by styrene-butadiene-styrene (SBS), polyethylene (PE) and ethylene-vinyl-acetate (EVA) copolymers. The order degree of the carbonite mesophase was analyzed using a polarizing microscope test, Fourier transform infrared spectroscopy and X-ray diffraction to screen out the most suitable copolymer type and addition amount. Furthermore, the mechanism of modification by this copolymer was analyzed. The results showed that adding SBS, PE and EVA to coal tar would affect the order of carbonaceous mesophase; however, at an addition rate of 10.0 wt.%, the linear-structure SBS copolymer with a styrene/butadiene ratio (S/B) of 30/70 exhibited the optimal degree of ordering in the carbonaceous mesophase. Its foam carbon prepared by polymer modification is the only one that forms a graphitized structure, with d002 of 0.3430 nm, and the maximum values of Lc and La are 3.54 nm and 2.22 nm, respectively. This is because, under elevated pressure and high-temperature conditions, SBS underwent chain scission, releasing a more significant number of methyl and other free radicals that interacted with the coal tar constituents. As a result, it reduced the affinity density of heavy coal tar molecules, enhanced fluidity, promoted the stacking of condensed aromatic hydrocarbons and increased the content of soluble carbonaceous mesophase, ultimately leading to a more favorable alignment of the carbonaceous mesophase. Full article
(This article belongs to the Special Issue Carbon/Polymer Composite Materials)
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Graphical abstract
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<p>(<b>a</b>) Infrared spectra of coal tar; (<b>b</b>) <sup>1</sup>H−NMR spectra of coal tar.</p>
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<p>Polarization diagrams of carbonaceous mesophase prepared with SBS with different structures ((<b>A</b>)—MPS<sub>1301</sub>, (<b>B</b>)—MPS<sub>791</sub>, (<b>C</b>)—MPS<sub>801</sub>, (<b>D</b>)—MPS<sub>4303</sub>).</p>
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<p>Polarization diagrams of carbonaceous mesophase prepared with SBS with different block ratios ((<b>A</b>)—MPS<sub>792</sub>, (<b>B</b>)—MPS<sub>1301</sub>, (<b>C</b>)—MPS<sub>791</sub>).</p>
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<p>Polarization diagrams of carbonaceous mesophase prepared with different SBS-1301 additions (<b>A</b>)—MPS<sub>1301-2</sub>, (<b>B</b>)—MPS<sub>1301-4</sub>, (<b>C</b>)—MPS<sub>1301-6</sub>, (<b>D</b>)—MPS<sub>1301-8</sub>, (<b>E</b>)—MPS<sub>1301-10</sub>).</p>
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<p>Polarization diagram of carbonaceous mesophase prepared by three kinds of PE density modification ((<b>A</b>)—MPP<sub>1</sub>, (<b>B</b>)—MPP<sub>2</sub>, (<b>C</b>)—MPP<sub>3</sub>).</p>
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<p>Polarization diagram of carbonaceous mesophase prepared with different addition amounts of HDPE ((<b>A</b>)—MPP<sub>1-2</sub>, (<b>B</b>)—MPP<sub>1-4</sub>, (<b>C</b>)—MPP<sub>1-6</sub>, (<b>D</b>)—MPP<sub>1-8</sub>, (<b>E</b>)—MPP<sub>1-10</sub>).</p>
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<p>Polarization diagram of carbonaceous mesophase modified by EVA with five different amounts of VA (<b>A</b>)—MPE<sub>1</sub>, (<b>B</b>)—MPE<sub>2</sub>, (<b>C</b>)—MPE<sub>3</sub>, (<b>D</b>)—MPE<sub>4</sub>, (<b>E</b>)—MPE<sub>5</sub>).</p>
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<p>Polarization diagrams of mesophase pitch prepared with different amounts of VA40-EVA ((<b>A</b>)—MPE<sub>40-2</sub>, (<b>B</b>)—MPE<sub>40-4</sub>, (<b>C</b>)—MPE<sub>40-6</sub>, (<b>D</b>)—MPE<sub>40-8</sub>, (<b>E</b>)—MPE<sub>40-10</sub>).</p>
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<p>(<b>a</b>) XRD spectra of graphitized foam carbon prepared with different copolymer-modified carbonaceous mesophases; (<b>b</b>) preparation of graphitized foam carbon d<sub>002,</sub> Lc and La from different copolymer-modified carbonaceous mesophases.</p>
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<p>(<b>a</b>) XRD spectrogram analysis of carbonaceous mesophase with different SBS; (<b>b</b>) analysis of different SBS-modified carbonaceous mesophase d<sub>002</sub>, Lc and La; (<b>c</b>) XRD spectrogram analysis of modified coal-tar-based mesophase with different SBS-1301; (<b>d</b>) analysis of carbon mesophase d<sub>002</sub>, Lc and La modified by different SBS-1301 content.</p>
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<p>(<b>a</b>) FT−IR plot of the effect of different SBS modifications on the coal-tar-based mesophase; (<b>b</b>) FT−IR diagram of the impact of further SBS-1301 additions on the carbonaceous mesophase.</p>
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<p>Mechanism diagram of SBS-modified preparation of carbonaceous mesophase.</p>
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14 pages, 4955 KiB  
Article
Prediction Models of Mechanical Properties of Jute/PLA Composite Based on X-ray Computed Tomography
by Xintao Zhao, Junteng Li, Shangbin Su and Ning Jiang
Polymers 2024, 16(1), 160; https://doi.org/10.3390/polym16010160 - 4 Jan 2024
Viewed by 1291
Abstract
The tensile strength and modulus of elasticity of a jute/polylactic acid (PLA) composite were found to vary nonlinearly with the loading angle of the specimen through the tensile test. The variation in these properties was related to the fiber orientation distribution (FOD) and [...] Read more.
The tensile strength and modulus of elasticity of a jute/polylactic acid (PLA) composite were found to vary nonlinearly with the loading angle of the specimen through the tensile test. The variation in these properties was related to the fiber orientation distribution (FOD) and fiber length distribution (FLD). In order to study the effects of the FOD and FLD of short fibers on the mechanical properties and to better predict the mechanical properties of short-fiber composites, the true distribution of short fibers in the composite was accurately obtained using X-ray computed tomography (XCT), in which about 70% of the jute fibers were less than 300 μm in length and the fibers were mainly distributed along the direction of mold flow. The probability density functions of the FOD and FLD were obtained by further analyzing the XCT data. Strength and elastic modulus prediction models applicable to short-fiber-reinforced polymer (SFRP) composites were created by modifying the laminate theory and the rule of mixtures using the probability density functions of the FOD and FLD. The experimental measurements were in good agreement with the model predictions. Full article
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<p>Process of short jute/PLA composite preparation: (<b>a</b>) Jute fiber; (<b>b</b>) Preparation of jute/PLA composite materials with 10% jute fiber content; (<b>c</b>) Cutting jute/PLA composite materials into particles; (<b>d</b>) Pour the dry composite particles into the injection molding machine; (<b>e</b>) Tensile specimens.</p>
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<p>Tensile specimens and specimens for XCT: (<b>a</b>) five groups of loading angle specimens; (<b>b</b>) specimen size for tensile testing; (<b>c</b>) X-ray tomography observation area; (<b>d</b>) XCT image.</p>
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<p>The jute/PLA 3D reconstruction process: (<b>a</b>) orthogonal images of the microstructure of the jute/PLA composite; (<b>b</b>–<b>d</b>) showing the fiber distribution in three sections; (<b>e</b>) 3D view; (<b>f</b>) threshold segmentation process; (<b>g</b>) separation of jute fibers; (<b>h</b>) jute fiber skeletonization process.</p>
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<p>Quantitative analysis of jute fibers: (<b>a</b>) definition of fiber polar coordinates (<span class="html-italic">θ</span>, <span class="html-italic">φ</span>) and loading orientation angles (<span class="html-italic">α</span>, <span class="html-italic">β</span>); (<b>b</b>) fiber length distribution; (<b>c</b>) fiber <span class="html-italic">θ</span> orientation distribution; (<b>d</b>) fiber <span class="html-italic">φ</span> orientation distribution; (<b>e</b>) fiber length distribution variation; (<b>f</b>) fiber <span class="html-italic">θ</span> orientation distribution angle variation; (<b>g</b>) fiber <span class="html-italic">φ</span> orientation distribution angle variation.</p>
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<p>Variation in fiber axial stress with fiber length. The blue area represents the fiber axial stress and the red line represents the ultimate fiber strength.</p>
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<p>Simplified model of short-fiber composites: (<b>a</b>) the true form of short fibers in the matrix; (<b>b</b>) short-fiber composites at the same <span class="html-italic">g</span>(<span class="html-italic">θ</span>) and <span class="html-italic">φ</span> = 0; (<b>c</b>) laminate with the same fiber length and the same fiber direction.</p>
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<p>Variation in the modulus of elasticity of the composite with the angle <span class="html-italic">α</span> in the direction of force: comparison of experimental and theoretical values.</p>
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<p>Diagram of the fiber structure passing through the plane of the crack: (<b>a</b>) the fibers are parallel to the load loading direction; (<b>b</b>) the fibers make an angle <span class="html-italic">θ</span> with the normal of the crack plane.</p>
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<p>Comparison between tensile strength prediction and experimental results.</p>
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15 pages, 5102 KiB  
Article
Synthesis of High-Value Bio-Based Polyamide 12,36 Microcellular Foams with Excellent Dimensional Stability and Shape Recovery Properties
by Chin-Wen Chen, Palraj Ranganathan, Bhuvanenthiran Mutharani, Jia-Wei Shiu, Syang-Peng Rwei, Yen-Hsiang Chang and Fang-Chyou Chiu
Polymers 2024, 16(1), 159; https://doi.org/10.3390/polym16010159 - 4 Jan 2024
Cited by 2 | Viewed by 1407
Abstract
The search for alternatives to petroleum-based thermoplastic polyamide elastomers (TPAEs) has recently drawn great interest. In this study, a bio-massed TPAE, PA12,36, was synthesized using 1,12-dodecanediamine (DDA) and fatty dimer acid (FDA, PripolTM1009) precursors via catalyst and solvent-free melt polycondensation. The [...] Read more.
The search for alternatives to petroleum-based thermoplastic polyamide elastomers (TPAEs) has recently drawn great interest. In this study, a bio-massed TPAE, PA12,36, was synthesized using 1,12-dodecanediamine (DDA) and fatty dimer acid (FDA, PripolTM1009) precursors via catalyst and solvent-free melt polycondensation. The molecular structure and molecular weight of the PA12,36 were characterized by 1H NMR, FTIR, and GPC. PA12,36 displayed a low melting temperature of 85.8 °C, an initial degradation temperature of 425 °C, and a glass-transition temperature of 30.4 °C, whereas it sustained satisfactory tensile strength (10.0 MPa) and superior strain at break (1378%). Furthermore, PA12,36 was foamed by supercritical CO2, and the cell size, cell density, and porosity were determined. The entangled long-chained FDA component generated a physically crosslinked network, which promoted the melt viscosity of PA12,36 against elongations of foam cell growth and increased foamability significantly. As a result, uniform structured cellular foams with a cell diameter of 15–24 µm and high cell density (1011 cells/cm3–1012 cells/cm3) were successfully achieved. The foaming window was widened from 76 to 81 °C, and the expansion ratio was increased from 4.8 to 9.6. Additionally, PA12,36 foam with a physically crosslinked structure presented a better creep shape recovery percentage (92–97.9%) and sturdier dimensional stability. This bio-based PA12,36 foam is a promising candidate to replace petroleum-based thermoplastic elastomer foams for engineering applications, particularly shoe soles. Full article
(This article belongs to the Special Issue Advances in Polymeric Foams)
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<p>(<b>a</b>) Photograph of the synthesized, compression-molded, transparent PA12,36 and (<b>b</b>) FTIR spectrographs of FDA and PA12,36.</p>
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<p><sup>1</sup>H NMR spectrographs of FDA and PA12,36.</p>
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<p>(<b>a</b>) The DSC heating and cooling curves and (<b>b</b>) TGA (blue) and DTG (red) curves of PA12,36.</p>
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<p>(<b>a</b>) storage modulus (<span class="html-italic">E</span>′) and (<b>b</b>) tan <span class="html-italic">δ</span> trace of PA12,36.</p>
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<p>(<b>a</b>) Tensile s-s curve and (<b>b</b>) photograph of PA12,36 tensile test specimen.</p>
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<p>(<b>a</b>) CO<sub>2</sub> absorption of PA12,36 at different S<sub>pressure</sub>s and (<b>b</b>) CO<sub>2</sub> absorption of PA12,36 at 79 °C.</p>
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<p>Different magnification SEM cellular micrographs of PA12,36 foams prepared under various T<sub>foaming</sub>s: (<b>a</b>–<b>c</b>) 76 °C, (<b>d</b>–<b>f</b>) 79 °C, and (<b>g</b>–<b>i</b>) 81 °C.</p>
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<p>(<b>a</b>) E<sub>R</sub>, (<b>b</b>) porosity, (<b>c</b>) average cell diameter (<span class="html-italic">D</span>), and (<b>d</b>) cell density of PA12,36 foams prepared at different T<sub>foaming</sub>s (S<sub>pressure</sub> = 150 bar, F<sub>time</sub> = 90 min).</p>
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<p>Cyclic creep recovery traces of PA12,36 foams prepared under different T<sub>foaming</sub>s: (<b>a</b>) 76 °C, (<b>b</b>) 79 °C, and (<b>c</b>) 81 °C; (<b>d</b>) Creep recovery percentage of PA12,36 foams prepared under different T<sub>foaming</sub>s.</p>
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<p>Photographs of PA12,36 foams prepared at different T<sub>faoming</sub>s and the dimensional stability of the foams at different periods.</p>
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<p>Synthesis of PA12,36 from the polycondensation of DDA and FDA.</p>
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13 pages, 6273 KiB  
Article
In Situ Polymerization of Antibacterial Modification Polyamide 66 with Au@Cu2O-ZnO Ternary Heterojunction
by Xiang Li, Mi Zheng, Shikun Zhao, Zhiwen Cao, Kai Pan, Xinxing Feng, Hua Zhang, Min Zheng and Cheng Wang
Polymers 2024, 16(1), 158; https://doi.org/10.3390/polym16010158 - 4 Jan 2024
Viewed by 1416
Abstract
In situ polymerization has proven to be an effective route through which to introduce function materials into polyamide materials. In this work, a nano-heterojunction material was evenly dispersed in PA66 via in situ polymerization methods to yield the antimicrobial PA66. The composites showed [...] Read more.
In situ polymerization has proven to be an effective route through which to introduce function materials into polyamide materials. In this work, a nano-heterojunction material was evenly dispersed in PA66 via in situ polymerization methods to yield the antimicrobial PA66. The composites showed excellent antibacterial activity against Staphylococcus aureus and Escherichia coli, with strong mechanical properties. Fourier transform infrared spectroscopy (FTIR) showed that metal ions reacted with oxygen-containing functional groups. In addition, the shift of oxygen peaks in XPS spectra confirmed the occurrence of a complexation reaction. X-ray diffraction (XRD) and differential scanning calorimetry (DSC) confirmed the effect of nano-heterojunction, which induced crystallization. Scanning electron microscopy (SEM) and transmission electron microscopy (TEM) showed uniform dispersion of heterojunctions in PA66. Tensile testing revealed decreased toughness with higher loadings. The nanocomposite polyamide material has good processing properties which can be processed into thin films, molds, and wires without changing the morphology, and can be widely used in a variety of fields. Full article
(This article belongs to the Section Polymer Composites and Nanocomposites)
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<p>The preparation of PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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<p>(<b>a</b>) TEM image of Au@Cu<sub>2</sub>O heterostructures; (<b>b</b>) TEM image of Au@Cu<sub>2</sub>O@ZnO ternary heterojunction; (<b>c</b>) SEM image of Au@Cu<sub>2</sub>O@ZnO ternary heterojunction.</p>
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<p>SEM images of fracture sections: (<b>a</b>) pure PA66; (<b>b</b>) 400 ppm; (<b>c</b>) 800 ppm; (<b>d</b>) 1200 ppm.</p>
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<p>TEM images of fracture sections: (<b>a</b>) PA66/Au@Cu<sub>2</sub>O-ZnO; (<b>b</b>–<b>e</b>) elemental mapping images of (<b>c</b>) Cu, (<b>d</b>) Au, and (<b>e</b>) Zn corresponding to (<b>b</b>) Au@Cu<sub>2</sub>O-ZnO compositions.</p>
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<p>(<b>a</b>) FTIR spectrums of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites; (<b>b</b>) relative viscosities of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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<p>C 1s and O 1s XPS spectra of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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<p>DSC heating curves (<b>a</b>) and cooling curves (<b>b</b>) of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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<p>XRD patterns of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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<p>TG and DTG curves of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites under N<sub>2</sub>: (<b>a</b>) TG curves; (<b>b</b>) DTG curves.</p>
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<p>Yield strength and elongation at break of PA66 and PA66/Au@Cu<sub>2</sub>O-ZnO composites.</p>
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13 pages, 2320 KiB  
Article
Theoretical and Experimental Research Concerning the Friction Forces Developed in Hydraulic Cylinder Coaxial Sealing Systems Made from Polymers
by Flavius Aurelian Sârbu, Felix Arnăuţ, Andrea Deaconescu and Tudor Deaconescu
Polymers 2024, 16(1), 157; https://doi.org/10.3390/polym16010157 - 4 Jan 2024
Cited by 1 | Viewed by 1154
Abstract
Optimizing the energy efficiency of hydraulic cylinder modern sealing systems requires, among other things, minimizing the developed friction forces. This can be achieved by manufacturing seals from polymer-based polytetrafluoroethylene-type materials (Virgin PTFE and filled PTFE) or from thermoplastic polyurethane elastomers. This paper presents [...] Read more.
Optimizing the energy efficiency of hydraulic cylinder modern sealing systems requires, among other things, minimizing the developed friction forces. This can be achieved by manufacturing seals from polymer-based polytetrafluoroethylene-type materials (Virgin PTFE and filled PTFE) or from thermoplastic polyurethane elastomers. This paper presents a procedure for calculating and experimentally determining the friction forces developed in the coaxial sealing systems of hydraulic cylinders pistons. Three sealing systems made from different materials were tested under varying conditions of pressure and velocity on an experimental test stand set up by the authors. The paper concludes with data and recommendations for the selection of the optimum seal material in order to maximize energy efficiency. Our comparative research conducted on the seal materials led to the conclusion that for reducing friction forces in hydraulic cylinders, Virgin PTFE is the most adequate. Full article
(This article belongs to the Special Issue Polymer Materials for Sensors and Actuators)
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<p>Coaxial sealing systems.</p>
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<p>The formation of the fluid layer upon the onset of relative motion.</p>
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<p>The construction of the tested hydraulic cylinder.</p>
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<p>Dependency of the non-dimensional contact surface area on sealing ring material and pressure.</p>
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<p>Dimensions of the coaxial sealing systems.</p>
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<p>A diagram and an image of the test stand used for the determination of the friction forces.</p>
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<p>Variation in the total friction forces versus the velocity and the pressure of the sealed-off fluid.</p>
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<p>Variation in the friction forces in the case of a single coaxial sealing system.</p>
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11 pages, 1946 KiB  
Article
Rigidity with Flexibility: Porous Triptycene Networks for Enhancing Methane Storage
by Fei Guo, Hui Ma, Bin-Bin Yang, Zhen Wang, Xiang-Gao Meng, Jian-Hua Bu and Chun Zhang
Polymers 2024, 16(1), 156; https://doi.org/10.3390/polym16010156 - 4 Jan 2024
Viewed by 1247
Abstract
In the pursuit of advancing materials for methane storage, a critical consideration arises given the prominence of natural gas (NG) as a clean transportation fuel, which holds substantial potential for alleviating the strain on both energy resources and the environment in the forthcoming [...] Read more.
In the pursuit of advancing materials for methane storage, a critical consideration arises given the prominence of natural gas (NG) as a clean transportation fuel, which holds substantial potential for alleviating the strain on both energy resources and the environment in the forthcoming decade. In this context, a novel approach is undertaken, employing the rigid triptycene as a foundational building block. This strategy is coupled with the incorporation of dichloromethane and 1,3-dichloropropane, serving as rigid and flexible linkers, respectively. This combination not only enables cost-effective fabrication but also expedites the creation of two distinct triptycene-based hypercrosslinked polymers (HCPs), identified as PTN-70 and PTN-71. Surprisingly, despite PTN-71 manifesting an inferior Brunauer–Emmett–Teller (BET) surface area when compared to the rigidly linked PTN-70, it showcases remarkably enhanced methane adsorption capabilities, particularly under high-pressure conditions. At a temperature of 275 K and a pressure of 95 bars, PTN-71 demonstrates an impressive methane adsorption capacity of 329 cm3 g−1. This exceptional performance is attributed to the unique flexible network structure of PTN-71, which exhibits a pronounced swelling response when subjected to elevated pressure conditions, thus elucidating its superior methane adsorption characteristics. The development of these advanced materials not only signifies a significant stride in the realm of methane storage but also underscores the importance of tailoring the structural attributes of hypercrosslinked polymers for optimized gas adsorption performance. Full article
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<p>Synthesis of PTN-70 and PTN-71.</p>
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<p>SEM and TEM images of PTN-70 (<b>a</b>,<b>b</b>) and PTN-71 (<b>c</b>,<b>d</b>). Scale bar: 5 μm (<b>a</b>) and 1 μm (<b>b</b>–<b>d</b>).</p>
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<p>Nitrogen sorption isotherms of PTN-70 and PTN-71 at 77 K (<b>a</b>), pore size distributions calculated using NLDFT methods (<b>b</b>). (<b>c</b>) Methane (273 K) isotherm of PTN-70 and PTN-71. (<b>d</b>) Methane adsorption of PTN-70 and PTN-71 up to 95 bars at 273 K.</p>
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<p>Adsorption capacity of methane for various materials recently reported. Details are located in <a href="#app1-polymers-16-00156" class="html-app">Table S1 of the Supplementary Materials</a>.</p>
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23 pages, 24830 KiB  
Article
Self-Healing Properties of Water Tree Damage in Multilayered Shell–Core-Structured Microcapsules/Cross-Linked Polyethylene Composites
by Bo Zhu, Hao Sun, Yaqi Zhu, Shengkun He and Ximu Han
Polymers 2024, 16(1), 155; https://doi.org/10.3390/polym16010155 - 4 Jan 2024
Cited by 1 | Viewed by 1220
Abstract
To investigate the effect of the structure of microcapsules on the properties of cross-linked polyethylene (XLPE) composites, three XLPE specimens filled with multilayered shell–core-structured microcapsules are designed. In this paper, the microcapsules are first analyzed morphologically and chemically. In addition, the effect of [...] Read more.
To investigate the effect of the structure of microcapsules on the properties of cross-linked polyethylene (XLPE) composites, three XLPE specimens filled with multilayered shell–core-structured microcapsules are designed. In this paper, the microcapsules are first analyzed morphologically and chemically. In addition, the effect of the microcapsule structure on the typical electrical properties of the composites is explored. Finally, the self-healing ability of XLPE specimens filled with microcapsules is verified. The results show that the SiO2 on the surface of the trilayer shell–core microcapsules can make the microcapsules and the XLPE matrix have a better mechanical interlocking ability, which makes the typical properties of the trilayer shell–core microcapsules slightly better than those of the bilayer shell–core microcapsules. Moreover, when the bilayer shell–core or trilayer shell–core microcapsules rupture under the action of an electric field, the repair material reacts with the water tree under capillary action to consume the residual water while generating organic matter to fill in the cavity, thus repairing the damaged area of the water tree and ultimately achieving the self-healing of the composite water tree. Full article
(This article belongs to the Topic Polymers for Electrical Systems)
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<p>(<b>a</b>) Internal structure of the monolayer shell–core microcapsules. (<b>b</b>) Internal structure of the bilayer shell–core microcapsules. (<b>c</b>) Internal structure of the trilayer shell–core microcapsules. (<b>d</b>) Schematic diagram of the water tree aging experimental device.</p>
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<p>(<b>a</b>) Internal structure of the monolayer shell–core microcapsules. (<b>b</b>) Internal structure of the bilayer shell–core microcapsules. (<b>c</b>) Internal structure of the trilayer shell–core microcapsules. (<b>d</b>) Schematic diagram of the water tree aging experimental device.</p>
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<p>Microscopic morphologies of the microcapsules with multilayered shell–core structures: (<b>a</b>) OM photograph of the monolayer shell–core microcapsule; (<b>b</b>) SEM photograph of the monolayer shell–core microcapsule; (<b>c</b>) OM photograph of the bilayer shell–core microcapsule; (<b>d</b>) SEM photograph of the bilayer shell–core microcapsule; (<b>e</b>) OM photograph of the trilayer shell–core microcapsule; (<b>f</b>) SEM photograph of the trilayer shell–core microcapsule.</p>
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<p>Microscopic morphologies of the microcapsules with multilayered shell–core structures: (<b>a</b>) OM photograph of the monolayer shell–core microcapsule; (<b>b</b>) SEM photograph of the monolayer shell–core microcapsule; (<b>c</b>) OM photograph of the bilayer shell–core microcapsule; (<b>d</b>) SEM photograph of the bilayer shell–core microcapsule; (<b>e</b>) OM photograph of the trilayer shell–core microcapsule; (<b>f</b>) SEM photograph of the trilayer shell–core microcapsule.</p>
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<p>(<b>a</b>) Particle size distribution of microcapsules; (<b>b</b>) infrared spectra of microcapsules with multilayered shell–core structure.</p>
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<p>DSC temperature spectra of XLPE specimens filled with multilayered shell–core–structured microcapsules: (<b>a</b>) the melting process; (<b>b</b>) the crystallization process.</p>
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<p>Weibull distribution of the AC breakdown field strength of the XLPE specimens filled with multilayered shell–core-structured microcapsules.</p>
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<p>(<b>a</b>) Relative dielectric constants of the XLPE specimens filled with multilayered shell–core-structured microcapsules. (<b>b</b>) Dielectric loss factor of XLPE specimens filled with multilayered shell–core-structured microcapsules.</p>
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<p>The space charge distribution map of the XLPE specimens filled with multilayered shell–core–structured microcapsules: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell−core microcapsules; (<b>c</b>) bilayer shell−core microcapsules; (<b>d</b>) trilayer shell−core microcapsules.</p>
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<p>The space charge distribution map of the XLPE specimens filled with multilayered shell–core–structured microcapsules: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell−core microcapsules; (<b>c</b>) bilayer shell−core microcapsules; (<b>d</b>) trilayer shell−core microcapsules.</p>
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<p>The OM microstructure of the 30-day aging water tree area of the sample: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell–core microcapsules; (<b>c</b>) bilayer shell–core microcapsules; (<b>d</b>) trilayer shell–core microcapsules.</p>
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<p>The OM microstructure of the 30-day aging water tree area of the sample: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell–core microcapsules; (<b>c</b>) bilayer shell–core microcapsules; (<b>d</b>) trilayer shell–core microcapsules.</p>
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<p>The SEM observation results of the 30-day aging water tree area of the sample: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell–core microcapsules; (<b>c</b>) bilayer shell–core microcapsules; (<b>d</b>) trilayer shell–core microcapsules.</p>
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<p>The SEM observation results of the 30-day aging water tree area of the sample: (<b>a</b>) no microcapsules; (<b>b</b>) monolayer shell–core microcapsules; (<b>c</b>) bilayer shell–core microcapsules; (<b>d</b>) trilayer shell–core microcapsules.</p>
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<p>Schematic diagram of the water tree aging self-healing principle.</p>
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<p>Reaction of the repair solution with water at room temperature.</p>
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<p>Depolarization current of XLPE specimens filled with microcapsules.</p>
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<p>The simulation model of the water tree area.</p>
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<p>Electric field distribution of the water tree area before and after repair.</p>
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16 pages, 20703 KiB  
Article
Influence of Electrospinning Parameters on the Morphology of Electrospun Poly(3-hydroxybutyrate-co-3-hydroxyvalerate) Fibrous Membranes and Their Application as Potential Air Filtration Materials
by Yaohui Liu, Yanming Wang, Cheng-Hao Lee, Chi-Wai Kan and Xiaoying Lu
Polymers 2024, 16(1), 154; https://doi.org/10.3390/polym16010154 - 4 Jan 2024
Cited by 5 | Viewed by 1526
Abstract
A large number of non-degradable materials have severely damaged the ecological environment. Now, people are increasingly pursuing the use of environmentally friendly materials to replace traditional chemical materials. Polyhydroxyalkonates (PHAs) are receiving increasing attention because of the unique biodegradability and biocompatibility they offer. [...] Read more.
A large number of non-degradable materials have severely damaged the ecological environment. Now, people are increasingly pursuing the use of environmentally friendly materials to replace traditional chemical materials. Polyhydroxyalkonates (PHAs) are receiving increasing attention because of the unique biodegradability and biocompatibility they offer. However, the applications of PHAs are still limited due to high production costs and insufficient study. This project examines the optimal electrospinning parameters for the production of PHA-based fibrous membranes for air filtration. A common biodegradable polyester, Poly(3-hydroxybutyrate-co-3-hydroxyvalerate) (PHBV), was electrospun into a nanofibrous membrane with a well-controlled surface microstructure. In order to produce smooth, bead-free fibers with micron-scale diameters, the effect of the process parameters (applied electric field, solution flow rate, inner diameter of hollow needle, and polymer concentration) on the electrospun fiber microstructure was optimized. The well-defined fibrous structure was optimized at an applied electric field of 20 kV, flow rate of 0.5 mL/h, solution concentration of 12 wt.%, and needle inner diameter of 0.21 mm. The morphology of the electrospun PHBV fibrous membrane was observed by scanning electron microscopy (SEM). Fourier transform infrared (FTIR) and Raman spectroscopy were used to explore the chemical signatures and phases of the electrospun PHBV nanofiber. The ball burst strength (BBS) was measured to assess the mechanical strength of the membrane. The small pore size of the nanofiber membranes ensured they had good application prospects in the field of air filtration. The particle filtration efficiency (PFE) of the optimized electrospun PHBV fibrous membrane was above 98% at standard atmospheric pressure. Full article
(This article belongs to the Section Polymer Applications)
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<p>Chemical structure of Poly(3-hydroxybutyrate-co-3-hydroxyvalerate) (PHBV).</p>
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<p>Schematic diagram of the electrospinning process.</p>
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<p>SEM images of the electrospun PHBV nanofibers at an applied voltage of (<b>a</b>) 9 kV, (<b>b</b>) 12 kV, (<b>c</b>) 18 kV, and (<b>d</b>) 20 kV.</p>
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<p>SEM images of the electrospun PHBV nanofibers at a solution injection flow rate of (<b>a</b>) 0.5 mL/h, (<b>b</b>) 1 mL/h, (<b>c</b>) 3 mL/h, and (<b>d</b>) 5 mL/h.</p>
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<p>SEM images of the electrospun PHBV nanofibers under the effect of a capillary inner diameter of (<b>a</b>) 0.5 mm, (<b>b</b>) 0.33 mm, (<b>c</b>) 0.21 mm, and (<b>d</b>) 0.16 mm.</p>
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<p>SEM images of the electrospun PHBV nanofibers prepared at (<b>a</b>) 12 wt.%, (<b>b</b>) 13 wt.%, and (<b>c</b>) 14 wt.%. of PHBV in chloroform.</p>
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<p>FTIR spectrum of PHBV (<b>a</b>) before electrospinning and (<b>b</b>) after electrospinning.</p>
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<p>Raman spectra of PHBV electrospun fibrous membrane.</p>
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<p>(<b>a</b>) The appearance of ball burst apparatus used to examine the mechanical strength and stiffness of the fabric. (<b>b</b>) Ball burst (load−elongation) curves of the PHBV fibrous membrane and ASTM F2100 level 3 surgical mask.</p>
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<p>Particle filtration efficiency of electrospun PHBV membrane (PFE: 98.9%) and ASTM F2100 level 3 mask (PFE:99.0%).</p>
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21 pages, 8274 KiB  
Article
Preparation and Performance of Bitumen Modified by Melt-Blown Fabric of Waste Mask Based on Grey Relational and Radar Chart Analysis
by Peifeng Cheng, Chunmeng Zheng, Zhanming Zhang, Yiming Li, Kai Huang, Dezhong Yu and Yongcheng Ji
Polymers 2024, 16(1), 153; https://doi.org/10.3390/polym16010153 - 3 Jan 2024
Cited by 1 | Viewed by 1306
Abstract
To effectively utilize waste mask materials in road engineering and minimize resource waste, the melt-blown fabric (MBF) of waste masks was utilized to modify the virgin bitumen. The preparation process of MBF-modified bitumen was investigated, and the physical and rheological properties of bitumen [...] Read more.
To effectively utilize waste mask materials in road engineering and minimize resource waste, the melt-blown fabric (MBF) of waste masks was utilized to modify the virgin bitumen. The preparation process of MBF-modified bitumen was investigated, and the physical and rheological properties of bitumen were measured. Subsequently, the blending mechanism during preparation and the dispersion morphology of the modifier were explored. Finally, the pavement performance of the mixture was investigated, and a radar chart analysis was performed to quantitatively assess the effects of MBF modification. Results suggested that the recommended preparation process of shear time, shear rate, and shear temperature was 170 °C, 4000 r/min, and 15 min, respectively. MBF enhanced the high-temperature stability of the binder and weakened the temperature susceptibility. The modification was primarily a physical process. No network structure and agglomeration formed in the bitumen after modification. The addition of MBF significantly improved the resistance of the asphalt mixture to a high-temperature deformation and water damage but harmed its low-temperature crack resistance. The comprehensive assessment results of 0% (f1), 1% (f2), 3% (f3), and 5% (f4) MBF to improve the properties of the mixture were in the following order: f3>f4>f2>f1, where the impact of 3% MBF was the most significant, followed by 5% and 1% MBF. Full article
(This article belongs to the Section Polymer Processing and Engineering)
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<p>(<b>a</b>) Production process of MBF; (<b>b</b>) MBF pieces; (<b>c</b>) SEM images of pieces.</p>
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<p>DSC results of MBF.</p>
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<p>Preparation process of samples.</p>
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<p>Test process and results of MSCR test.</p>
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<p>Aggregate gradation of AC-16.</p>
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<p>Sketch map of RCEM.</p>
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<p>Samples prepared in the study.</p>
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<p>Results of physical property tests.</p>
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<p>Results of TS test.</p>
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<p>Results of MSCR test.</p>
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<p>Results of MSCR test.</p>
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<p>Changing of Jnr and R at 64 °C.</p>
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<p>Results of BBR test.</p>
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<p>FTIR spectra of the samples.</p>
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<p>FM image of the bitumen.</p>
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<p>Results of high-temperature stability tests.</p>
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<p>Results of moisture susceptibility tests.</p>
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<p>Radar charts of RCEM results.</p>
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13 pages, 3853 KiB  
Article
Epoxy-Acrylic Polymer In-Situ Filling Cell Lumen and Bonding Cell Wall for Wood Reinforcement and Stabilization
by Yiliang Liu, Jilong Fan, Fengbiao Yao, Xudong Gao, Yueying Zhao, Baoxuan Liu, Xiaoying Dong and Yongfeng Li
Polymers 2024, 16(1), 152; https://doi.org/10.3390/polym16010152 - 3 Jan 2024
Cited by 1 | Viewed by 1250
Abstract
Under a global carbon-neutralizing environment, renewable wood is a viable alternative to non-renewable resources due to its abundance and high specific strength. However, fast-growing wood is hard to be applied extensively due to low mechanical strength and poor dimensional stability and durability. In [...] Read more.
Under a global carbon-neutralizing environment, renewable wood is a viable alternative to non-renewable resources due to its abundance and high specific strength. However, fast-growing wood is hard to be applied extensively due to low mechanical strength and poor dimensional stability and durability. In this study, epoxy-acrylic resin-modified wood was prepared by forming a functional monomer system with three monomers [glycidyl methacrylate (GMA), maleic anhydride (MAN), and polyethylene glycol-200-dimethylacrylic acid (PEGDMA)] and filling into the wood cell cavity. The results showed that in the case of an optimal monomer system of nGMA:nPEGDMA = 20:1 and an optimal MAN dosage of 6%, the conversion rate of monomers reached 98.01%, the cell cavity was evenly filled by the polymer, with the cell wall chemically bonded. Thus, a bonding strength of as high as 1.13 MPa, a bending strength of 112.6 MPa and an impact toughness of 74.85 KJ/m2 were applied to the modified wood, which presented excellent dimensional stability (720 h water absorption: 26%, and volume expansion ratio: 5.04%) and rot resistance (loss rates from white rot and brown rot: 3.05% and 0.67%). Additionally, polymer-modified wood also exhibited excellent wear resistance and heat stability. This study reports a novel approach for building new environmentally friendly wood with high strength and toughness and good structural stability and durability. Full article
(This article belongs to the Special Issue Wood Polymer Composites: Properties, Processing and Applications)
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<p>Schematic diagram of epoxy-acrylic polymer-modified (through in situ filling) aspen wood realizing compatibility of interface bonding and high performance.</p>
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<p>Optimization of monomer ratio based on the interfacial bonding strength between three kinds of man-made board substrates and modified veneer: optimization of GMA/PEGDMA ratio based on (<b>a</b>) paticleboard, (<b>b</b>) fiberboard and (<b>c</b>) plywood; optimization of MAN dosage based on (<b>d</b>) paticleboard, (<b>e</b>) fiberboard and (<b>f</b>) plywood; microstructure of the bonding interface of modified veneered (<b>g</b>) paticleboard, (<b>h</b>) fiberboard and (<b>i</b>) plywood at the optimal ratio.</p>
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<p>Dimensional stability and rot resistance of epoxy-acrylic polymer-modified wood: (<b>a</b>) comparison of resin conversion rate between monomer system and wood impregnated in other resins, (<b>b</b>) SEM microstructure of the cross-section of the modified wood, (<b>c</b>) FTIR curves of modified wood and unmodified wood, (<b>d</b>) water absorption rate, (<b>e</b>) water absorption volume expansion rate and (<b>f</b>) anti-expansion rate, (<b>g</b>) rot resistance value of modified wood and unmodified wood, (<b>h</b>) SEM microstructure of unmodified wood after wood preservation test, (<b>i</b>) SEM microstructure of modified wood after wood preservation test (the inner illustration is the image of modified wood not corroded by rot fungi in the wood preservation test).</p>
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<p>Impact toughness of polymer-modified wood: (<b>a</b>) XRD curves of polymer-modified wood and unmodified wood, (<b>b</b>) schematic diagram of impact toughness test, (<b>c</b>) comparison of impact toughness between polymer-modified wood and unmodified wood and (<b>d</b>) SEM microstructure of impact fracture surface of polymer-modified wood.</p>
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<p>Mechanical properties and heat stability of polymer-modified wood: (<b>a</b>) bending strength, (<b>b</b>) compressive strength (rift grain), (<b>c</b>) hardness, (<b>d</b>) wear value, (<b>e</b>) TG curves and (<b>f</b>) DTG curves.</p>
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17 pages, 4037 KiB  
Article
Preparation of Cationic Polyacrylamide Suspension and Its Application in Oilfield Wastewater Treatment
by Zhongjin Wei, Wenjun Long, Shaohua Li, Yu Zhao, Siting Yu and Fengshan Zhou
Polymers 2024, 16(1), 151; https://doi.org/10.3390/polym16010151 - 3 Jan 2024
Cited by 2 | Viewed by 1993
Abstract
Cationic polyacrylamide (CPAM) solid particle is one of the most commonly used organic polymer flocculants in oilfield wastewater treatment, but it poses some problems, such as a slow dissolution rate and an easy formation into a “fish-eye” in the process of diluting into [...] Read more.
Cationic polyacrylamide (CPAM) solid particle is one of the most commonly used organic polymer flocculants in oilfield wastewater treatment, but it poses some problems, such as a slow dissolution rate and an easy formation into a “fish-eye” in the process of diluting into aqueous solution. However, the current liquid CPAM products also have some problems, such as low effective content, poor storage stability, degradation in a short time, and high preparation costs. In this paper, a CPAM suspension was successfully prepared with 50.00% CPAM fine powder, 46.87% oil phase solvent, 0.63% separating agent, 1.56% emulsifying and dispersing agent, and 0.94% rheology modifier. This suspension has an effective content of 50.00%. It also showed no separation in 7 days of storage at room temperature, no separation in 30 min of centrifugation at a speed of 2000 rpm, and diluted to a 0.40% solution in just 16.00 min. For 1000 NTU of diatomite-simulated wastewater, the optimal turbidity removal rate of the suspension was 99.50%, which was higher than the optimal turbidity removal rate of 98.40% for the inorganic flocculant polymeric aluminum chloride (PAC). For oilfield wastewater, the optimal turbidity removal rate of the CPAM suspension was 35.60%, which was higher than the optimal turbidity removal rate of 28.40% for solid particle CPAM. In a scale-up test, the CPAM suspension achieved a good application effect. Full article
(This article belongs to the Special Issue Recent Advances in Functional Polymer Materials for Water Treatment)
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<p>Schematic diagram of the CPAM suspension preparation.</p>
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<p>The adsorption mechanism of F-Silica.</p>
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<p>Effects of F-Silica: (<b>a</b>) trend of the apparent viscosity of the suspension (at 50% effective content of the suspension); (<b>b</b>) trend of dissolution time (dilution concentrations of 0.20% and 0.40%).</p>
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<p>Effects of emulsifying and dispersing agent: (<b>a</b>) dissolution time (dilution concentration of 0.40%); (<b>b</b>) synergistic effect of CTAB and Span 80 (dilution concentration of 0.40%).</p>
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<p>Effects of the rheology modifier: (<b>a</b>) suspension separation rate (centrifuged at 2000 rpm for 30 min); (<b>b</b>) dissolution time (dilution concentration of 0.40%); (<b>c</b>) room temperature storage; (<b>d</b>) mechanism of shear force enhancement.</p>
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<p>Image of the suspension under an optical microscope: (<b>a</b>) 200× magnification; (<b>b</b>) 400× magnification.</p>
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<p>Comparison of flocculation and water purification performance of different products: (<b>a</b>) simulated wastewater (organic polymer flocculant, dilution concentrations of 0.20%); (<b>b</b>) simulated wastewater (inorganic flocculant, dilution concentrations of 10.00%); (<b>c</b>) oilfield wastewater (dilution concentrations of 0.20%); (<b>d</b>) water purification effect.</p>
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<p>The wastewater treatment process for the wastewater station.</p>
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<p>Field dosing situation: (<b>a</b>) CPAM particle dosing tank; (<b>b</b>) CPAM suspension dosing tank; (<b>c</b>) CPAM suspension for dilution; (<b>d</b>) after full dissolution.</p>
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<p>Wastewater before and after field dosing: (<b>a</b>) wastewater in the air flotation machine before dosing; (<b>b</b>) wastewater in the air flotation machine after dosing; (<b>c</b>) wastewater at the outlet before dosing; (<b>d</b>) wastewater at the outlet after dosing.</p>
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10 pages, 6467 KiB  
Article
Flexible Film Bulk Acoustic Wave Filter Based on Poly(vinylidene fluoride-trifluorethylene)
by Xiangyu He, Jiaqi Lu, Feng Gao, Shurong Dong, Juan Li, Hao Jin and Jikui Luo
Polymers 2024, 16(1), 150; https://doi.org/10.3390/polym16010150 - 3 Jan 2024
Cited by 2 | Viewed by 1158
Abstract
Poly(vinylidene fluoride-trifluorethylene) (P(VDF-TrFE)) has promising potential applications in radio-frequency filters due to their excellent piezoelectric properties, flexibility, and stability. In this paper, a flexible film bulk acoustic wave filter is investigated based on P(VDF-TrFE) as piezoelectric film. A new method based on three-step [...] Read more.
Poly(vinylidene fluoride-trifluorethylene) (P(VDF-TrFE)) has promising potential applications in radio-frequency filters due to their excellent piezoelectric properties, flexibility, and stability. In this paper, a flexible film bulk acoustic wave filter is investigated based on P(VDF-TrFE) as piezoelectric film. A new method based on three-step annealing is developed to efficiently remove the porosity inside the P(VDF-TrFE) films so as to improve its properties. The obtained film achieved high β-phase content beyond 80% and a high piezoelectric coefficient of 27.75 pm/V. Based on the low porosity β-phase films, a flexible wide-band RF filter is designed, which consists of a bulk acoustic wave resonator and lumped inductor-capacitor elements as a hybrid configuration. The resonator sets the filter’s center frequency, while the lumped LC-based matching network extends the bandwidth and enhances out-of-band rejection. The testing results of the proposed wide-band filter show its good performance, with 12.5% fractional bandwidth and an insertion loss of 3.1 dB. To verify the possibility of folding and stacking the flexible bulk acoustic wave devices for high-density multi-filter integration in MIMO communication, bending tests of the filter are also conducted with the bending strain range up to 5500 με. The testing results show no noticeable performance degradation after four bending cycles. This work demonstrates the potential of β-phase P(VDF-TrFE) bulk acoustic wave filters to expand the scope of future flexible radio-frequency filter applications. Full article
(This article belongs to the Special Issue Research Progress of Polymer-Based Sensors)
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<p>The fabrication process of the P(VDF-TrFE) thin films.</p>
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<p>P(VDF-TrFE) Thin Films: (<b>a</b>) sample S1 cross-section; (<b>b</b>) sample S2 cross-section (<b>c</b>) XRD curves of sample S1 and S2; (<b>d</b>) FTIR spectra of sample S1 and S2; (<b>e</b>) amplitude versus applied voltage of piezoresponse hysteresis loops in P(VDF-TrFE) films; (<b>f</b>) phase versus applied voltage.</p>
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<p>(<b>a</b>) Schematic diagram of the structure of the P(VDF-TrFE) BAW Resonators; (<b>b</b>) simulated S11 and Z curves of P(VDF-TrFE) BAW with 20 μm P(VDF-TrFE) film.</p>
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<p>(<b>a</b>) A photo and drawing of the fabricated P(VDF-TrFE) BAW; S11 and Z spectra of (<b>b</b>) the BAW with a 70 μm P(VDF-TrFE) film; (<b>c</b>) with a 20 μm P(VDF-TrFE) film; (<b>d</b>) with a 10 μm P(VDF-TrFE) film, respectively.</p>
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<p>The proposed P(VDF-TrFE) BAW filter. (<b>a</b>) Circuit diagram for the proposed BAW filter; (<b>b</b>) a photo of the fabricated filter.</p>
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<p>(<b>a</b>) The frequency response of fabricated P(VDF-TrFE) BAW filter; (<b>b</b>) matching networks and the parallel inductor.</p>
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<p>The flexible P(VDF−TrFE) BAW filter (<b>a</b>) performance of resonator under different strains; (<b>b</b>) performance of filter under different strains; (<b>c</b>) bending testing.</p>
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25 pages, 4751 KiB  
Article
Cellulose Functionalization Using N-Heterocyclic-Based Leaving Group Chemistry
by Arvind Negi and Ali R. Tehrani-Bagha
Polymers 2024, 16(1), 149; https://doi.org/10.3390/polym16010149 - 3 Jan 2024
Cited by 2 | Viewed by 1927
Abstract
There has been continuous interest in developing novel activators that facilitate the functionalization of cellulosic materials. In this paper, we developed a strategy in which trisubstituted triazinium salts act as cellulose preactivators. As leaving groups, these triazinium salts utilize N-heterocycles (pyridine, imidazole, [...] Read more.
There has been continuous interest in developing novel activators that facilitate the functionalization of cellulosic materials. In this paper, we developed a strategy in which trisubstituted triazinium salts act as cellulose preactivators. As leaving groups, these triazinium salts utilize N-heterocycles (pyridine, imidazole, and nicotinic acid). Initially, we optimized the synthetic route for developing these novel cellulose preactivators (triazinium salts), whose structures were confirmed using NMR spectroscopy. The surface zeta potential of cellulose changed from a negative value to a positive one after preactivation due to the cationic nature of these preactivators. To enhance the scope of the study, we functionalized the cellulose-preactivated materials with a series of amine- or hydroxy-containing aliphatic and aromatic hydrocarbons, nucleophilic amino acids (cysteine), colorants (2-aminoanthraquinone and 2-amino-3-methyl-anthraquinone), and biopolymer (zein protein). The treated samples were analyzed using FTIR, time-gated Raman spectroscopy, and reflection spectroscopy, and the success of the functionalization process was validated. To widen the scope of such chemistries, we synthesized four reactive agents containing N-heterocyclic-based leaving groups (pyridine and nicotinic acid) and successfully functionalized cellulose with them in one step. The proposed single- and two-step functionalization approaches will provide opportunities for chemically linking various chemical compounds to cellulose for different applications. Full article
(This article belongs to the Special Issue Advances in Natural Cellulose)
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<p>The chemical structures of (<b>A</b>) synthesized preactivators (PrAct-1, PrAct-2, and PrAct-3), (<b>B</b>) synthesized activators (Act-1, Act-2, Act-3, and Act-4), (<b>C</b>) cationizing agents used to study the optimization and strength of preactivators, and (<b>D</b>) amine-containing colorants.</p>
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<p>(<b>a</b>). Chemical reactivity: compared zeta potentials of preactivators with cellulose, including the zeta potential of the cellulose samples after reaction with preactivators at various concentrations. The zeta potential of the untreated cellulose sample was −9.63 mV. (<b>b</b>). A comparison of FTIR dips of nontreated cellulose with PrAct-3-treated cellulose (showing COOH stretching, C=C aromatic stretching, C-H stretching, and O-H stretching).</p>
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<p>Raman spectral characterization of (<b>A</b>) cotton fabric; (<b>B</b>) localized fiber (in focus) irradiated with a 532 nm laser; (<b>C</b>) time-gated 3D spectra of zein-treated cotton fabric; and (<b>D</b>) Raman spectral characterization of zein-treated cotton fabric extracted in the 5.1–5.3 ns range.</p>
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<p>Raman spectral characterization of (<b>A</b>) cotton fabric; (<b>B</b>) localized fiber (in focus) irradiated with a 532 nm laser; (<b>C</b>) time-gated 3D spectra of zein-treated cotton fabric; and (<b>D</b>) Raman spectral characterization of zein-treated cotton fabric extracted in the 5.1–5.3 ns range.</p>
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<p>(<b>a</b>) Time-gated Raman spectra of 1,5-pentadiol-treated cotton fabric, (<b>b</b>) time-gated Raman spectra of 1-Napthol-treated cotton fabric, (<b>c</b>) comparative FTIR spectra of PrAct-3 preactivated cellulose fabric, Act-1, and Act-4-activated cellulose fabric with aromatic hydrocarbon-functionalized cellulose fabric.</p>
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<p>FTIR spectra of nonactivated cellulose fiber (right-hand side) and Act-1-treated cellulose fiber (left-hand side).</p>
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<p>Cellulose functionalizations. (<b>A</b>). Two-step approach. (<b>B</b>). One-step approach.</p>
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<p>Synthetic route devised for the development of preactivators and side products.</p>
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<p>Structural features indicating the numbering of atoms for <sup>3</sup>J<sub>HH</sub> COSY, <sup>1</sup>H-NMR, and <sup>13</sup>C-NMR, and the correlation of vicinal protons in PrAct-1 (<b>A</b>–<b>C</b>), PrAct-2 (<b>D</b>–<b>F</b>), and PrAct-3 (<b>G</b>–<b>I</b>).</p>
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<p>Synthesis routes of four reactive chemicals (Act-1, Act-2, Act-3, and Act-4).</p>
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17 pages, 4838 KiB  
Article
Mucoadhesive Hybrid System of Silk Fibroin Nanoparticles and Thermosensitive In Situ Hydrogel for Amphotericin B Delivery: A Potential Option for Fungal Keratitis Treatment
by Pratthana Chomchalao, Nuttawut Saelim, Supaporn Lamlertthon, Premnapa Sisopa and Waree Tiyaboonchai
Polymers 2024, 16(1), 148; https://doi.org/10.3390/polym16010148 - 3 Jan 2024
Cited by 4 | Viewed by 1739
Abstract
The purpose of this work was to investigate the feasibility of a novel ophthalmic formulation of amphotericin B-encapsulated silk fibroin nanoparticles incorporated in situ hydrogel (AmB-FNPs ISG) for fungal keratitis (FK) treatment. AmB-FNPs ISG composites were successfully developed and have shown optimized physicochemical [...] Read more.
The purpose of this work was to investigate the feasibility of a novel ophthalmic formulation of amphotericin B-encapsulated silk fibroin nanoparticles incorporated in situ hydrogel (AmB-FNPs ISG) for fungal keratitis (FK) treatment. AmB-FNPs ISG composites were successfully developed and have shown optimized physicochemical properties for ocular drug delivery. Antifungal effects against Candida albicans and in vitro ocular irritation using corneal epithelial cells were performed to evaluate the efficacy and safety of the composite formulations. The combined system of AmB-FNPs-ISG exhibited effective antifungal activity and showed significantly less toxicity to HCE cells than commercial AmB. In vitro and ex vivo mucoadhesive tests demonstrated that the combination of silk fibroin nanoparticles with in situ hydrogels could enhance the adhesion ability of the particles on the ocular surface for more than 6 h, which would increase the ocular retention time of AmB and reduce the frequency of administration during the treatment. In addition, AmB-FNP-PEG ISG showed good physical and chemical stability under storage condition for 90 days. These findings indicate that AmB-FNP-PEG ISG has a great potential and be used in mucoadhesive AmB eye drops for FK treatment. Full article
(This article belongs to the Special Issue Development and Application of Bio-Based Polymers)
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<p>Average viscosity vs. temperature profiles of AmB-FNPs ISG.</p>
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<p>Stability of AmB-FNP-PEG-F127 ISG and AmB-FNP-PEG-F127/HA ISG under storage conditions (4 °C). (<b>a</b>) Visual appearance and (<b>b</b>) drug remaining of AmB in the formulations at different time points (mean ± SD, <span class="html-italic">n</span> = 3).</p>
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<p>The antifungal activity of AmB deoxycholate, standard AmB, AmB-FNPs, and AmB-FNPs ISG against <span class="html-italic">C. albicans</span> according to the agar well diffusion technique. * Significant at <span class="html-italic">p</span> &lt; 0.05 compared with AmB deoxycholate.</p>
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<p>The in vitro mucoadhesive properties of FITC-labeled FNPs and FITC-FNP-ISG. (<b>a</b>) %FITC remaining on the mucus membrane of FITC solution compared with three types of FITC-FNP dispersion; (<b>b</b>) %FITC remaining of FITC-FNP dispersion; (<b>c</b>) %FITC remaining of FITC-FNP-PEI dispersion; and (<b>d</b>) %FITC remaining of FITC-FNP-PEG dispersion compared with their in situ hydrogel composites.</p>
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<p>Ex vivo mucoadhesive studies of the nanoparticles and in situ hydrogel compared with nanodispersion and solution formulations. The fluorescence images of the remaining fluorescence on the cross-sectional porcine cornea after treatment with FITC solution (<b>a</b>–<b>d</b>), FITC-labeled FNP-PEG (<b>e</b>–<b>h</b>), FNP-PEG-F127 ISG (<b>i</b>–<b>l</b>), and FNP-PEG-F127/HA ISG (<b>m</b>–<b>p</b>) under continuous flow of STF at different time points (200×).</p>
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<p>In vitro cytotoxicity study of prepared formulations. (<b>a</b>) Percentage of HCE cell viability after 12 h incubation with AmB deoxycholate and AmB-FNP formulations (equivalent concentration of AmB at 5, 15, and 150 μg/mL). (<b>b</b>) Percentage of HCE cell viability after 12 h incubation with AmB-FNPs embedded in F127 and F127/HA in situ hydrogel (formulation dose at 150 μg/mL of AmB). (mean ± SD, <span class="html-italic">n</span> = 9, * <span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Morphology of HCE cells after exposure to AmB-FNP dispersions compared with the controls for 12 h: (<b>a</b>) untreated cells; (<b>b</b>) vehicle control; (<b>c</b>) 150 μg/mL AmB deoxycholate; (<b>d</b>) 150 μg/mL AmB-FNP; (<b>e</b>) 150 μg/mL AmB-FNP-PEI; and (<b>f</b>) 150 μg/mL AmB-FNP-PEG (200×).</p>
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<p>Morphology of HCE cells after exposure to AmB-FNPs ISG compared with their hydrogel bases for 12 h: (<b>a</b>) F127 ISG base; (<b>b</b>) AmB-FNP-F127; (<b>c</b>) AmB-FNP-PEI F127; (<b>d</b>) AmB-FNP-PEG F127; (<b>e</b>) F127/HA ISG base; (<b>f</b>) AmB-FNP-F127/HA; (<b>g</b>) AmB-FNP-PEI-F127/HA; and (<b>h</b>) AmB-FNP-PEG-F127/HA (200×).</p>
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17 pages, 6974 KiB  
Article
A Global Approach to Modeling Injection Molding
by Przemysław Narowski and Krzysztof Wilczyński
Polymers 2024, 16(1), 147; https://doi.org/10.3390/polym16010147 - 3 Jan 2024
Viewed by 2210
Abstract
A problem of modeling plastic injection forming (molding) is presented, including both the plasticizing system of the injection-forming machine and the mold. When modeling the plastic flow in the mold, the input quantities are essentially unknown, e.g., the plastic melt temperature. Thus, a [...] Read more.
A problem of modeling plastic injection forming (molding) is presented, including both the plasticizing system of the injection-forming machine and the mold. When modeling the plastic flow in the mold, the input quantities are essentially unknown, e.g., the plastic melt temperature. Thus, a comprehensive (global) model of the injection-forming process is needed for the flow in the plasticizing system and in the mold. The process output quantities from the plasticizing system will be the input quantities for the mold. When modeling the plastic flow in the injection-forming machine, a comprehensive approach should be applied to consider the solid material conveying, material plasticizing, and the material melt flow. The model of material plasticizing is a basis for building such global models. In this research, the effect of the flow (including plasticizing) in the injection-forming machine on the flow in the mold is studied by simulation (using Moldex3D 2023R3OR 64-bit software) and experimentation. These studies are carried out for the injection forming of selected material using a specialized spiral mold. Simulations performed with the use of Moldex3D software for the plasticizing system significantly improved the accuracy of the simulation of the flow in the mold. However, the best results were obtained using experimental data (plastic melt temperature) as input quantities for mold filling simulations. The novel concepts of injection-forming process modeling based on our previous experimentations are also discussed. Full article
(This article belongs to the Special Issue Injection Molding Process in Polymer Processing)
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<p>Injection forming: (<b>A</b>)—injection (filling), (<b>B</b>)—holding (packing), (<b>C</b>)—plasticizing (melting), (<b>D</b>)—mold opening (part ejection); 1—part (molding), 2—mold cavity, 3—cooling channels, 4—screw, 5—heaters, 6—hopper, 7—drive system (with permission from Rheology in Polymer Processing. Modeling and Simulation by K. Wilczyński; Carl Hanser Verlag: Munich 2021 [<a href="#B1-polymers-16-00147" class="html-bibr">1</a>]).</p>
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<p>The plasticizing phenomenon at single-screw extrusion with flood feeding (PP) [<a href="#B12-polymers-16-00147" class="html-bibr">12</a>].</p>
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<p>The effect of screw speed on polymer flow in the injection molding process at the plasticization stroke h<sub>plast</sub> = 1D and the backpressure P<sub>back</sub> = 0 MPa: (<b>a</b>) N = 100 rpm, (<b>b</b>) N = 300 rpm [<a href="#B45-polymers-16-00147" class="html-bibr">45</a>].</p>
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<p>The plasticizing phenomenon at single-screw extrusion with metered feeding (PP) [<a href="#B12-polymers-16-00147" class="html-bibr">12</a>].</p>
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<p>Spiral mold.</p>
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<p>Viscosity curve [<a href="#B39-polymers-16-00147" class="html-bibr">39</a>].</p>
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<p>Simulation of plastic flow in the injection-forming machine (bulk temperature) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa.</p>
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<p>Simulation of plastic flow in the injection-forming machine (pressure) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa.</p>
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<p>Simulation of plastic flow in the injection-forming machine (solid bed profile) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa.</p>
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<p>The influence of screw rotation N on the melt temperature at a backpressure of P<sub>back</sub> = 17 MPa.</p>
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<p>The influence of screw rotation N on the melt temperature at a backpressure of P<sub>back</sub> = 34 MPa.</p>
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<p>The influence of screw rotation N on the melt temperature at a backpressure of P<sub>back</sub> = 51 MPa.</p>
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<p>Spiral molding (part) and simulations (filling time) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa: (<b>a</b>) spiral molding, (<b>b</b>) A—simulation, (<b>c</b>) B—simulation, (<b>d</b>) C—simulation.</p>
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<p>Simulations (melt front temperature) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa: (<b>a</b>) A—simulation, (<b>b</b>) B—simulation, (<b>c</b>) C—simulation.</p>
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<p>Simulations (total velocity) obtained at a screw rotation speed of N = 175 rpm and a backpressure of P<sub>back</sub> = 34 MPa: (<b>a</b>) A—simulation, (<b>b</b>) B—simulation, (<b>c</b>) C—simulation.</p>
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<p>The influence of screw speed N on spiral length at a backpressure of P<sub>back</sub> = 17 MPa.</p>
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<p>The influence of screw speed N on spiral length at a backpressure of P<sub>back</sub> = 34 MPa.</p>
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<p>The influence of screw speed N on spiral length at a backpressure of P<sub>back</sub> = 51 MPa.</p>
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15 pages, 4422 KiB  
Article
Influence of Dilution on the Mechanical Properties and Microstructure of Polyurethane-Cement Based Composite Surface Coating
by Chao Xie, Yufeng Shi, Ping Wu, Binqiang Sun and Yaqiang Yue
Polymers 2024, 16(1), 146; https://doi.org/10.3390/polym16010146 - 3 Jan 2024
Cited by 2 | Viewed by 1119
Abstract
Polyurethane-cement composite are widely used in modern civil engineering, and the method of adding diluent is often used to adjust the construction process to adapt to the engineering environment. Studies have shown that the addition of diluent impacts the performance of polyurethane-cement based [...] Read more.
Polyurethane-cement composite are widely used in modern civil engineering, and the method of adding diluent is often used to adjust the construction process to adapt to the engineering environment. Studies have shown that the addition of diluent impacts the performance of polyurethane-cement based composite surface coatings, but there have been few reports on the influence of diluent content on the mechanical properties and microstructure of the coatings. To address this, polyurethane coatings with different diluent contents were prepared, and positron annihilation lifetime spectroscopy was used to test the microstructure of the coatings. The tensile strength and elongation at rupture were tested using a universal material testing machine, and the fracture interface morphology of each coating was observed by scanning electron microscopy. Finally, the correlation between the microstructure parameters and the mechanical properties of the coating was analyzed using grey relation theory. The results demonstrated that with the increase in diluent content, (i) the average radius of the free volume hole (R) and the free volume fraction (FV) of the coating both showed a trend of first decreasing and then increasing. The value of R was between 3.04 and 3.24 Å, and the value of FV was between 2.08 and 2.84%. (ii) The tensile strength of the coating increased first and then decreased, while the elongation at rupture decreased first and then increased. Among them, the value of tensile strength was between 3.23 and 4.02 MPa, and the value of elongation at fracture was between 49.34 and 63.04%. In addition, the free volume in polymers plays a crucial role in facilitating the migration of molecular chain segments and is closely related to the macroscopic mechanical properties of polymers. A correlation analysis showed that the R value of the coating had the greatest influence on its tensile strength, while FV showed a higher correlation with the elongation at rupture. Full article
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<p>Tensile strength test.</p>
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<p>Sandwich structure formed by the clamps.</p>
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<p>Positional relationship between the sample and scintillator detector.</p>
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<p>PALS spectrum of each sample.</p>
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<p>Each coating <span class="html-italic">o</span>-Ps annihilate spectrum fitting coefficient.</p>
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<p>Each coating <span class="html-italic">o</span>-Ps annihilate life and annihilation intensity.</p>
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<p>Results of free-volume parameters for samples.</p>
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<p>Test results of mechanical properties of each sample.</p>
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<p>The stress–strain curve of each sample.</p>
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<p>Cross-section SEM image of (<b>a</b>) S-10, (<b>b</b>) S-15, (<b>c</b>) S-20, (<b>d</b>) S-25, and (<b>e</b>) S-30.</p>
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<p>Correlation between mechanical properties and microstructure parameters of coating: (<b>a</b>) tensile strength and <span class="html-italic">R</span>, (<b>b</b>) tensile strength and <span class="html-italic">F<sub>V</sub></span>, (<b>c</b>) elongation at rupture and <span class="html-italic">R</span>, and (<b>d</b>) elongation at rupture and <span class="html-italic">F<sub>V</sub></span>.</p>
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13 pages, 3226 KiB  
Article
Polysaccharides Produced by Plant Growth-Promoting Rhizobacteria Strain Burkholderia sp. BK01 Enhance Salt Stress Tolerance to Arabidopsis thaliana
by Enni Chen, Changsheng Yang, Weiyi Tao and Shuang Li
Polymers 2024, 16(1), 145; https://doi.org/10.3390/polym16010145 - 3 Jan 2024
Cited by 4 | Viewed by 1680
Abstract
Salt stress is one of the most serious abiotic stresses leading to reduced agricultural productivity. Polysaccharides from seaweed have been used as biostimulants to promote crop growth and improve plant resistance to abiotic stress. In this study, PGPR strain Burkholderia sp. BK01 was [...] Read more.
Salt stress is one of the most serious abiotic stresses leading to reduced agricultural productivity. Polysaccharides from seaweed have been used as biostimulants to promote crop growth and improve plant resistance to abiotic stress. In this study, PGPR strain Burkholderia sp. BK01 was isolated from the rhizosphere of wheat, and it was characterized for phosphorus (Pi) dissolution, indole-3-acetic acid (IAA) production, ammonia (NH3) and exopolysaccharides (EPS). In particular, strain BK01 can efficiently produce extracellular polysaccharide with a yield of 12.86 g/L, using sorbitol as carbon source. BK01 EPS was identified as an heteropolysaccharide with Mw 3.559 × 106 Da, composed of (D)-galactose (75.3%), (D)-glucose (5.5%), (L)-rhamnose (5.5%), (D)-galactouronic acid (4.9%) and (D)-glucuronic acid (8.8%). The present work aims to highlight the effect of the BK01 EPS on growth and biochemical changes in Arabidopsis thaliana under salt stress (100 mM). The purified BK01 EPS at a concentration of 100 mg/L efficiently promoted the growth of plants in pot assays, improved the chlorophyll content, enhanced the activities of SOD, POD and CAT, and decreased the content of MDA. This results suggested that the polysaccharides produced by PGPR strain Burkholderia sp. BK01 can be used as biostimulants to promote plant growth and improve plant resistance to salt stress. Full article
(This article belongs to the Special Issue Natural Polysaccharides and Their Biological Applications)
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<p>Morphological characteristics and identification of <span class="html-italic">Burkholderia</span> sp. BK01. (<b>A</b>) Scanning electron micrograph of the strain BK01. (<b>B</b>) The colony morphology of the strain BK01. (<b>C</b>) Phylogenetic analysis of the isolate BK01 based on the sequencing of the 16S rDNA. The scale bar indicates 0.005 substitutions per nucleotide position.</p>
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<p>(<b>A</b>) Pi solubilization and pH in broth. (<b>B</b>) Yields of IAA produced by BK01. (<b>C</b>) Ammonia production tests of <span class="html-italic">Burkholderia</span> strains (1: <span class="html-italic">Burkholderia</span> sp. BK01; 2: <span class="html-italic">Burkholderia cepacia</span> ATCC 25416; 3. <span class="html-italic">Burkholderia</span> sp. CICC 24715). Values are three replicates.</p>
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<p>Yield of EPS, viscosity of fermentation broth, and biomass (OD<sub>600</sub>). Values are three replicates.</p>
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<p>Phenotypes of <span class="html-italic">Arabidopsis thaliana</span> after 7 days of NaCl treatment ((<b>A</b>), control; (<b>B</b>), 100 mM NaCl; (<b>C</b>), BKEPS 100 ppm + 100 mM NaCl; (<b>D</b>), BKEPS 100 ppm); on the far right is a seedling tray with uniform specifications.</p>
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<p>K<sup>+</sup>/Na<sup>+</sup> ratios in <span class="html-italic">Arabidopsis</span> seedlings under normal (CK and BKEPS) and salt stress (NaCl and BKEPS + NaCl) conditions. Values are the mean ± LSD of three replicates. Different letters indicate significant differences at <span class="html-italic">p</span> &lt; 0.05.</p>
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<p>MDA contents (<b>A</b>), and CAT (<b>B</b>), POD (<b>C</b>), SOD (<b>D</b>) activities in <span class="html-italic">Arabidopsis</span> seedlings. Values are the mean ± LSD of three replicates. Different letters indicate significant differences at <span class="html-italic">p</span> &lt; 0.05. MDA, malondialdehyde; SOD, superoxide dismutase; POD, peroxidase; CAT, catalase.</p>
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<p>Proline contents in <span class="html-italic">Arabidopsis</span> seedlings. Values are the mean ± LSD of three replicates. Different letters indicate significant differences at <span class="html-italic">p</span> &lt; 0.05.</p>
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22 pages, 5997 KiB  
Article
Poly(ethylene glycol) Methyl Ether Acrylate-Grafted Chitosan-Based Micro- and Nanoparticles as a Drug Delivery System for Antibiotics
by Corina-Lenuța Logigan, Christelle Delaite, Marcel Popa, Elena Simona Băcăiță, Crina Elena Tiron, Cristian Peptu and Cătălina Anișoara Peptu
Polymers 2024, 16(1), 144; https://doi.org/10.3390/polym16010144 - 2 Jan 2024
Cited by 3 | Viewed by 1796
Abstract
Nanotechnology is the science of creating materials at the nanoscale by using various devices, structures, and systems that are often inspired by nature. Micro- and nanoparticles (MPs, NPs) are examples of such materials that have unique properties and can be used as carriers [...] Read more.
Nanotechnology is the science of creating materials at the nanoscale by using various devices, structures, and systems that are often inspired by nature. Micro- and nanoparticles (MPs, NPs) are examples of such materials that have unique properties and can be used as carriers for delivering drugs for different biomedical applications. Chitosan (CS) is a natural polysaccharide that has been widely studied, but it has a problem with low water solubility at neutral or basic pH, which limits its processability. The goal of this work was to use a chemically modified CS with poly(ethylene glycol) methyl ether acrylate (PEGA) to prepare CS micronic and submicronic particles (MPs/NPs) that can deliver different types of antibiotics, respectively, levofloxacin (LEV) and Ciprofloxacin (CIP). The particle preparation procedure employed a double crosslinking method, ionic followed by a covalent, in a water/oil emulsion. The studied process parameters were the precursor concentration, stirring speeds, and amount of ionic crosslinking agent. MPs/NPs were characterized by FT-IR, SEM, light scattering granulometry, and Zeta potential. MPs/NPs were also tested for their water uptake capacity in acidic and neutral pH conditions, and the results showed that they had a pH-dependent behavior. The MPs/NPs were then used to encapsulate two separate drugs, LEV and CIP, and they showed excellent drug loading and release capacity. The MPs/NPs were also found to be safe for cells and blood, which demonstrated their potential as suitable drug delivery systems for biomedical applications. Full article
(This article belongs to the Section Polymer Networks)
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<p>MPs/NPs average diameter variation, µm.</p>
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<p>MPs/NPs Zeta potential values.</p>
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<p>FTIR spectra of sample P4 and CS-PEGA.</p>
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<p>Micrograph SEM of optimized MPs/NPs ionically crosslinked with Na<sub>2</sub>SO<sub>4</sub> (magnification graphical bar length P1–P7: 0.01 mm).</p>
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<p>Granulometric distribution curves of P1–P7 samples.</p>
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<p>Polymer concentration influence on the swelling process for P5 (0.35%); P4 (0.5%); P7 (0.75%).</p>
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<p>Stirring speed influence on the swelling process for MP/NP samples: P1 (5000 rpm); P2 (9000 rpm); P3 (12,000 rpm); P4 (15,000 rpm).</p>
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<p>MPs/NPs’ in vitro LEV release.</p>
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<p>MPs/NPs’ in vitro CIP release.</p>
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<p>The experimental data and the Weibull theoretical curve for levofloxacin (first row) and ciprofloxacin (second row).</p>
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<p>Influence of NPs on the Hemolysis Degree.</p>
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<p>Cell viability. (<b>A</b>). HMLE-Human mammary epithelial cells. (<b>B</b>). MDA-MB 231-Human mammary cancer cells. (<b>C</b>). 4T1-Mouse mammary cancer cells. (<b>D</b>). A549-Human Pulmonary cancer cells.</p>
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18 pages, 8634 KiB  
Article
Chemical Recycling of CFRP in an Environmentally Friendly Approach
by Asuka Sakai, Winarto Kurniawan and Masatoshi Kubouchi
Polymers 2024, 16(1), 143; https://doi.org/10.3390/polym16010143 - 2 Jan 2024
Cited by 1 | Viewed by 1613
Abstract
A novel and environmentally friendly recycling approach for carbon-fiber-reinforced plastics (CFRP) was studied using not only nitric acid (HNO3) but also our chosen alkaline, sodium hydrogen carbonate (NaHCO3). The CFRP specimen was first immersed into 8 M HNO3 [...] Read more.
A novel and environmentally friendly recycling approach for carbon-fiber-reinforced plastics (CFRP) was studied using not only nitric acid (HNO3) but also our chosen alkaline, sodium hydrogen carbonate (NaHCO3). The CFRP specimen was first immersed into 8 M HNO3 at 80 °C for 8 h, and then into 0.1 M NaHCO3 at 80 °C for 15 min to obtain resin-free recycled carbon fiber (rCFs). Using this new recycling method, it was shown that the recycling time was reduced to 8.3 h, whereas it originally took 24 h, as reported previously. It was shown that immersing the CFRP specimen into NaHCO3 caused a transesterification reaction with the remaining resin residue on the CF surface, which led to dissolving the resin into the NaHCO3 aqueous solution all at once. Additionally, NaHCO3 produced carbon dioxide gas while reacting with the resin residue; the CO2 gas physically helped removing the resin from the CF’s surface. Moreover, evaluating the physical properties of the rCFs demonstrated an improvement in fiber strength and adhesiveness to resin. Therefore, this recycling method was shown to be effective in recovering high-quality rCFs in a relatively short recycling period. Full article
(This article belongs to the Section Polymer Composites and Nanocomposites)
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<p>Decomposition and recovery process of carbon fiber from CFRP specimen. (<b>a</b>) Scheme-1: CFRP immersed in 8 M HNO<sub>3</sub> for 5~48 h; (<b>b</b>) Scheme-2: CFRP immersed in 8 M HNO<sub>3</sub> refreshed with HNO<sub>3</sub> for every 8 h; (<b>c</b>) Scheme-3~6: CFRP immersed in solution X after immersion in 8 M HNO<sub>3</sub> where solution X is NaOH, NaHCO<sub>3</sub>, sodium lauryl sulfate (SDS), poly ethylene glycol (PEG), and hexadecyltrimethylammonium bromide.</p>
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<p>The composition of CFRP used in this research.</p>
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<p>(<b>a</b>–<b>e</b>) Pictures of CFRP samples immersed in a test tube and the rCF collected under each solution condition described in each of the figures; (<b>f</b>) picture of vCF.</p>
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<p>Pictures of the recovered decomposed resins. Resin-A from HNO<sub>3</sub>, in which the CFRP was immersed for 24 h in Scheme-1; Resin-A’ from HNO<sub>3</sub>, in which the CFRP was immersed for 8 h in Scheme-1; Resin-B from NaOH (pH 8) in Scheme-3; and Resin-C from NaHCO<sub>3</sub> in Scheme-4.</p>
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<p>SEM images (SEI) of the surface of (<b>a</b>) vCF and (<b>b</b>–<b>g</b>) rCF-1~6, where the red circle represents the resin residues.</p>
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<p>Molecular weight distribution of Resin-A, -A’, -B, and -C, measured using SEC.</p>
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<p>Average molecular weight of decomposed resin recovered from HNO<sub>3</sub>.</p>
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<p>FT-IR spectra of decomposed resin measured using the KBr disk method.</p>
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<p>Schematic image of the decomposition and dissolution mechanisms of the epoxy resin with nitric acid and alkaline aqueous solutions.</p>
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<p>Schematic image of the mass balance of input and output through recycling process.</p>
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<p>Interfacial shear strength between carbon fiber and resin measured with microdroplet tests for a data plot with a resin droplet size of <span class="html-italic">L</span> = 70 μm for vCF and rCF-4.</p>
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<p>(<b>a</b>) Tensile strength and (<b>b</b>) tensile modulus of vCF and rCF-4 measured using a single-fiber fragmentation test.</p>
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<p>Calibration curve (molecular weight distribution of polystyrene measured with SEC).</p>
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<p>Intensity ratio of D1 band and G1 band obtained from Raman spectroscopy analysis measured on the surface of vCF and rCF-4.</p>
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16 pages, 3656 KiB  
Article
Improving the Sustainability of Catalytic Glycolysis of Complex PET Waste through Bio-Solvolysis
by Izotz Amundarain, Sheila López-Montenegro, Laura Fulgencio-Medrano, Jon Leivar, Ana Iruskieta, Asier Asueta, Rafael Miguel-Fernández, Sixto Arnaiz and Beñat Pereda-Ayo
Polymers 2024, 16(1), 142; https://doi.org/10.3390/polym16010142 - 2 Jan 2024
Cited by 7 | Viewed by 2983
Abstract
This work addresses a novel bio-solvolysis process for the treatment of complex poly(ethylene terephthalate) (PET) waste using a biobased monoethylene glycol (BioMEG) as a depolymerization agent in order to achieve a more sustainable chemical recycling process. Five difficult-to-recycle PET waste streams, including multilayer [...] Read more.
This work addresses a novel bio-solvolysis process for the treatment of complex poly(ethylene terephthalate) (PET) waste using a biobased monoethylene glycol (BioMEG) as a depolymerization agent in order to achieve a more sustainable chemical recycling process. Five difficult-to-recycle PET waste streams, including multilayer trays, coloured bottles and postconsumer textiles, were selected for the study. After characterization and conditioning of the samples, an evaluation of the proposed bio-solvolysis process was carried out by monitoring the reaction over time to determine the degree of PET conversion (91.3–97.1%) and bis(2-hydroxyethyl) terephthalate (BHET) monomer yield (71.5–76.3%). A monomer purification process, using activated carbon (AC), was also developed to remove the colour and to reduce the metal content of the solid. By applying this purification strategy, the whiteness (L*) of the BHET greatly increased from around 60 to over 95 (L* = 100 for pure white) and the Zn content was significantly reduced from around 200 to 2 mg/kg. The chemical structure of the purified monomers was analyzed via infrared spectroscopy (FTIR) and differential scanning calorimetry (DSC), and the composition of the samples was measured by proton nuclear magnetic resonance (1H-NMR), proving a high purity of the monomers with a BHET content up to 99.5% in mol. Full article
(This article belongs to the Section Biobased and Biodegradable Polymers)
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<p>Mechanism for glycolysis reaction [<a href="#B7-polymers-16-00142" class="html-bibr">7</a>].</p>
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<p>Conditioned complex PET waste samples.</p>
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<p>PET glycolysis reaction and product purification process.</p>
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<p>FTIR spectrum of (<b>a</b>) PET waste samples and (<b>b</b>) their ashes.</p>
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<p>Evolution of BHET yield versus PET/BioMEG molar ratio. Operating conditions: temperature = 185 °C, time= 2 h, stirring rate = 250 rpm and catalyst content = 1 wt.%. Feedstock: PET-1.</p>
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<p>Progress of the solvolysis reaction by means of (<b>a</b>) HPLC and (<b>b</b>) NMR. Operating conditions: temperature = 185 °C, PET/BioMEG = 1/7.6 (mol/mol), stirring rate = 250 rpm and catalyst content = 1 wt.%. Feedstock: PET-1.</p>
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<p>Effect of reaction time on (<b>a</b>) PET conversion and (<b>b</b>) BHET yield. Operating conditions: temperature = 185 °C, PET/BioMEG = 1/7.6 (mol/mol), stirring rate= 250 rpm and catalyst content = 1 wt.%.</p>
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<p>Characterization of BHET samples by means of (<b>a</b>) FTIR and (<b>b</b>) DSC. Operating conditions: temperature = 185 °C, time = 4 h, PET/BioMEG = 1/7.6 (mol/mol), stirring rate = 250 rpm and catalyst content = 1 wt.%.</p>
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<p>Molar composition of (<b>a</b>) unpurified and (<b>b</b>) purified BHET samples by NMR. Operating conditions: temperature = 185 °C, time = 4 h, PET/BioMEG = 1/7.6 (mol/mol), stirring rate = 250 rpm and catalyst content = 1 wt.%.</p>
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<p>NMR spectra of a purified BHET sample. Operating conditions: temperature = 185 °C, time = 4 h, PET/BioMEG = 1/7.6 (mol/mol), stirring rate = 250 rpm and catalyst content = 1 wt.%. Feedstock: PET-1.</p>
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50 pages, 7061 KiB  
Review
Fresh Properties, Strength, and Durability of Fiber-Reinforced Geopolymer and Conventional Concrete: A Review
by Osama Mohamed and Haya Zuaiter
Polymers 2024, 16(1), 141; https://doi.org/10.3390/polym16010141 - 1 Jan 2024
Cited by 10 | Viewed by 5308
Abstract
Reducing the environmental footprint of the construction industry in general and concrete in particular is essential. The addition of synthetic and natural fibers to concrete mixes at appropriate dosages enhances durability and strength and extends the lifespan of concrete infrastructures. This study reviews [...] Read more.
Reducing the environmental footprint of the construction industry in general and concrete in particular is essential. The addition of synthetic and natural fibers to concrete mixes at appropriate dosages enhances durability and strength and extends the lifespan of concrete infrastructures. This study reviews the geometric and mechanical properties of selected fibers such as steel, basalt, polypropylene, polyvinyl alcohol, polyethylene, glass, carbon, and natural fibers and their impact on concrete fresh, mechanical, and durability properties when combined in different configurations. The study focuses on the effect of blending fibers with concrete mixes that use alkali-activated binders based on recycled industrial byproducts such as slag and fly ash and thereby contribute to reduction of CO2 contribution through complete or partial replacement of Ordinary Portland cement (OPC). As a result, the effect of binder content, binder composition, alkaline activator concentration, and water-to-binder (w/b) ratio on fresh properties, mechanical strength, and durability of concrete with blended fibers is also evaluated in this study. The properties of fiber-reinforced concrete with alkali-activated binder and conventional OPC binders are compared. Fiber-reinforced concrete with alkali-activated binders that are based on industrial byproducts may represent sustainable alternatives to conventional concrete and offers competitive fresh and mechanical properties when fiber properties, fiber content, w/b ratio, binder type, and dosage are carefully considered in concrete mix design. Full article
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<p>Keywords map of highest relevance to the study using VOS viewer [<a href="#B44-polymers-16-00141" class="html-bibr">44</a>].</p>
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<p>Effect of carbon fiber content on the slump diameter of self-compacting concrete [<a href="#B32-polymers-16-00141" class="html-bibr">32</a>].</p>
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<p>Effect of polypropylene fiber content on the slump diameter of high-performance concrete containing OPC and microsilica [<a href="#B83-polymers-16-00141" class="html-bibr">83</a>].</p>
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<p>Effect of steel fiber content, fiber length, and activator ratio on the flow diameter of slag-based concrete (0%/2.5 = fiber content/Na<sub>2</sub>SiO<sub>3</sub>/NaOH) [<a href="#B14-polymers-16-00141" class="html-bibr">14</a>].</p>
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<p>Slump flow values of concretes with fibers across basalt volume fraction ranging from 0% to 0.5% [<a href="#B84-polymers-16-00141" class="html-bibr">84</a>].</p>
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<p>Slump values of concretes with and without reinforced fibers [<a href="#B15-polymers-16-00141" class="html-bibr">15</a>,<a href="#B17-polymers-16-00141" class="html-bibr">17</a>,<a href="#B20-polymers-16-00141" class="html-bibr">20</a>,<a href="#B36-polymers-16-00141" class="html-bibr">36</a>].</p>
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<p>Compressive strength of fiber-reinforced alkali-activated fly ash/slag concretes (ST0.4 = steel fiber content of 0.4%, PP0.4 = polypropylene fiber content of 0.4%, PVA0.4 = PVA fiber content of 0.4%) [<a href="#B33-polymers-16-00141" class="html-bibr">33</a>].</p>
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<p>Compressive strength of basalt fiber-reinforced fly ash-based concretes [<a href="#B37-polymers-16-00141" class="html-bibr">37</a>].</p>
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<p>Compressive strength of alkali-activated GGBS/fly ash concretes and mortars reinforced with different fibers [<a href="#B13-polymers-16-00141" class="html-bibr">13</a>,<a href="#B14-polymers-16-00141" class="html-bibr">14</a>,<a href="#B18-polymers-16-00141" class="html-bibr">18</a>,<a href="#B22-polymers-16-00141" class="html-bibr">22</a>,<a href="#B37-polymers-16-00141" class="html-bibr">37</a>,<a href="#B39-polymers-16-00141" class="html-bibr">39</a>,<a href="#B66-polymers-16-00141" class="html-bibr">66</a>].</p>
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<p>Flexural strength of fly ash-based concretes reinforced with polypropylene and steel fibers (PP0.5 = polypropylene fiber content of 0.5%, ST0.5 = steel fiber content of 0.5%) [<a href="#B13-polymers-16-00141" class="html-bibr">13</a>].</p>
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<p>The stress–strain curves for OPC and slag-based concrete reinforced with polypropylene and steel fibers after 28 days [<a href="#B90-polymers-16-00141" class="html-bibr">90</a>].</p>
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<p>Flexural behavior of self-compacting geopolymer concrete reinforced with steel fibers at NaOH concentrations of (<b>a</b>) 8 M and (<b>b</b>) 12 M (Control = without fiber reinforcement) [<a href="#B17-polymers-16-00141" class="html-bibr">17</a>].</p>
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<p>Flexural strength of fiber-reinforced concretes [<a href="#B12-polymers-16-00141" class="html-bibr">12</a>,<a href="#B13-polymers-16-00141" class="html-bibr">13</a>,<a href="#B14-polymers-16-00141" class="html-bibr">14</a>,<a href="#B17-polymers-16-00141" class="html-bibr">17</a>,<a href="#B18-polymers-16-00141" class="html-bibr">18</a>,<a href="#B33-polymers-16-00141" class="html-bibr">33</a>,<a href="#B37-polymers-16-00141" class="html-bibr">37</a>,<a href="#B39-polymers-16-00141" class="html-bibr">39</a>,<a href="#B54-polymers-16-00141" class="html-bibr">54</a>,<a href="#B66-polymers-16-00141" class="html-bibr">66</a>].</p>
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<p>Drying shrinkage of slag-based concretes reinforced with steel fibers (Control = without fibers, ST0.4 = steel fiber content of 0.4%, PP0.4 = polypropylene fiber content of 0.4%, PVA0.4 = PVA fiber content of 0.4%) [<a href="#B33-polymers-16-00141" class="html-bibr">33</a>].</p>
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<p>Water absorption of alkali-activated mortar reinforced with carbon fibers [<a href="#B32-polymers-16-00141" class="html-bibr">32</a>].</p>
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28 pages, 12285 KiB  
Article
A Novel Recyclable Magnetic Nano-Catalyst for Fenton-Photodegradation of Methyl Orange and Imidazole Derivatives Catalytic Synthesis
by Marzough A. Albalawi, Amira K. Hajri, Bassem Jamoussi and Omnia A. Albalawi
Polymers 2024, 16(1), 140; https://doi.org/10.3390/polym16010140 - 1 Jan 2024
Cited by 3 | Viewed by 1463
Abstract
A magnetite chlorodeoxycellulose/ferroferric oxide (CDC@Fe3O4) heterogeneous photocatalyst was synthesised via treated and modified cotton in two steps. The designed nanocomposites were characterised by FTIR, TGA, XRD, SEM, and VSM analyses. The Fenton-photocatalytic decomposition efficiency of the synthesised magnetic catalyst [...] Read more.
A magnetite chlorodeoxycellulose/ferroferric oxide (CDC@Fe3O4) heterogeneous photocatalyst was synthesised via treated and modified cotton in two steps. The designed nanocomposites were characterised by FTIR, TGA, XRD, SEM, and VSM analyses. The Fenton-photocatalytic decomposition efficiency of the synthesised magnetic catalyst was evaluated under visible sunlight using Methyl Orange (MO) as a model organic pollutant. The impacts of several degradation parameters, including the light source, catalyst load, irradiation temperature, oxidant dose, and pH of the dye aqueous solution and its corresponding concentration on the Fenton photodegradation performance, were methodically investigated. The (CDC@Fe3O4) heterogeneous catalyst showed a remarkable MO removal rate of 97.9% at 10 min under visible-light irradiation. (CDC@Fe3O4) nanomaterials were also used in a heterogeneous catalytic optimised protocol for a multicomponent reaction procedure to obtain nine tetra-substituted imidazole derivatives. The green protocol afforded imidazole derivatives in 30 min with good yields (91–97%) at room temperature and under ultrasound irradiation. Generally, a synthesised recyclable heterogeneous nano-catalyst is a good example and is suitable for wastewater treatment and organic synthesis. Full article
(This article belongs to the Special Issue Advanced Composite Materials for Water Contaminant Removal)
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Figure 1
<p>UV–Vis absorption of (CDC) and (CDC@Fe<sub>3</sub>O<sub>4</sub>) (<b>a</b>) and the corresponding bandgap data of (CDC@Fe<sub>3</sub>O<sub>4</sub>) (<b>b</b>).</p>
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<p>FTIR spectra of cotton, (CDC), and (CDC@Fe<sub>3</sub>O<sub>4</sub>).</p>
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<p>TGA curves of cotton, (CDC), and (CDC@Fe<sub>3</sub>O<sub>4</sub>).</p>
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<p>Magnetization versus applied field (M-H) curves for superparamagnetic Fe<sub>3</sub>O<sub>4</sub> (a) and ferrimagnetic CDC@Fe<sub>3</sub>O<sub>4</sub> (b).</p>
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<p>XRD patterns of (CDC) and (CDC@Fe<sub>3</sub>O<sub>4</sub>).</p>
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<p>SEM images of (CDC) (<b>a</b>) and (CDC@Fe<sub>3</sub>O<sub>4</sub>) (<b>b</b>).</p>
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<p>Variations in the MO removal rates under different light sources.</p>
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<p>Variations in the MO removal rates under different catalytic systems.</p>
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<p>Effect of (CDC@Fe<sub>3</sub>O<sub>4</sub>) load on MO removal rate.</p>
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<p>Effect of MO concentration on removal rates.</p>
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<p>Variations of MO removal rates under different pH values.</p>
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<p>Effect of [H<sub>2</sub>O<sub>2</sub>] concentration on MO removal rate.</p>
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<p>Effect of temperature on MO removal rate.</p>
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<p>MO UV-visible spectra exhibited an absorbance decrease at 468.8 nm within 10 min. Photographs showing vanishing colour during the photocatalytic treatment.</p>
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<p>Proposed Fenton-photocatalytic degradation mechanism.</p>
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<p>Varied effects of radical scavengers on MO degradation using US/H<sub>2</sub>O<sub>2</sub>/CDC @ Fe<sub>3</sub>O<sub>4</sub>.</p>
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<p>Five consecutive photocatalytic MO degradation processes of MO using (CDC@Fe<sub>3</sub>O<sub>4</sub>).</p>
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<p>Investigated and simulated chosen kinetic adsorption models: (<b>a</b>) intraparticle diffusion, (<b>b</b>) pseudo-second order, and (<b>c</b>) Elovich.</p>
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<p>Efficiency of the catalytic run (<b>a</b>) and SEM images (CDC@Fe<sub>3</sub>O<sub>4</sub>) after six runs (<b>b</b>).</p>
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<p>Synthesis of magnetic functionalised cotton.</p>
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<p>Schematic representation of imidazole derivative (A) synthesis.</p>
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<p>Proposed catalytic mechanism.</p>
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16 pages, 3516 KiB  
Article
Thermosensitive Chitosan Hydrogels: A Potential Strategy for Prolonged Iron Dextran Parenteral Supplementation
by Emerson Durán, Andrónico Neira-Carrillo, Felipe Oyarzun-Ampuero and Carolina Valenzuela
Polymers 2024, 16(1), 139; https://doi.org/10.3390/polym16010139 - 31 Dec 2023
Viewed by 1258
Abstract
Iron deficiency anemia (IDA) presents a global health challenge, impacting crucial development stages in humans and other mammals. Pigs, having physiological and metabolic similarities with humans, are a valuable model for studying and preventing anemia. Commonly, a commercial iron dextran formulation (CIDF) with [...] Read more.
Iron deficiency anemia (IDA) presents a global health challenge, impacting crucial development stages in humans and other mammals. Pigs, having physiological and metabolic similarities with humans, are a valuable model for studying and preventing anemia. Commonly, a commercial iron dextran formulation (CIDF) with iron dextran particles (IDPs) is intramuscularly administered for IDA prevention in pigs, yet its rapid metabolism limits preventive efficacy. This study aimed to develop and evaluate chitosan thermosensitive hydrogels (CTHs) as a novel parenteral iron supplementation strategy, promoting IDPs’ prolonged release and mitigating their rapid metabolism. These CTHs, loaded with IDPs (0.1, 0.2, and 0.4 g of theoretical iron/g of chitosan), were characterized for IM iron supplementation. Exhibiting thermosensitivity, these formulations facilitated IM injection at ~4 °C, and its significant increasing viscosity at 25–37 °C physically entrapped the IDPs within the chitosan’s hydrophobic gel without chemical bonding. In vitro studies showed CIDF released all the iron in 6 h, while CTH0.4 had a 40% release in 72 h, mainly through Fickian diffusion. The controlled release of CTHs was attributed to the physical entrapment of IDPs within the CTHs’ gel, which acts as a diffusion barrier. CTHs would be an effective hydrogel prototype for prolonged-release parenteral iron supplementation. Full article
(This article belongs to the Special Issue Research Progress on Chitosan Applications)
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Graphical abstract
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<p>Macroscopic appearance (<b>a</b>) and electron microscopy images (<b>b</b>) of the thermosensitive chitosan/iron dextran hydrogel formulations (CTHs) with increasing iron concentrations (0.1, 0.2, and 0.4 g of theoretical iron/g of chitosan).</p>
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<p>Macroscopic appearance of the chitosan thermosensitive hydrogel (CTH) formulations with increasing iron concentrations (0.1, 0.2, and 0.4 g of theoretical iron/g of chitosan) and the commercial iron dextran formulation (CIDF), showing the separation of the sol–gel phases at 37 °C before (<b>a</b>) and after (<b>b</b>) centrifugation. The white and black arrows indicate the upper (water) phase and the lower (gel) phase of CTH0, respectively; (<b>c</b>,<b>d</b>) show the appearance of CIDF and CTH0.4 injected at 37 °C into a piece of pork meat, respectively.</p>
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<p>Spectrograms of the chitosan thermosensitive hydrogel (CTH) formulations with increasing iron concentrations (0.1, 0.2, and 0.4 g of theoretical iron/g of chitosan), the commercial iron dextran formulation (CIDF), and precursors. Dotted lines mark the main absorption bands. Data obtained through infrared spectroscopy.</p>
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<p>Cumulative iron release from commercial iron dextran formulation (CIDF) and the chitosan thermosensitive hydrogel containing iron dextran particles (CTH0.4) at 37 °C. * Significative differences between formulation values for each measurement time (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Two-dimensional schematic representation of interactions among chitosan, glycerophosphate (GP), water, and the iron dextran particles (IDPs) in a chitosan thermosensitive hydrogel in sol state (<b>a</b>) and gel state (<b>b</b>). Dotted circles represent chitosan–GP ionic bonds, and yellow areas represent interactions involving GP–water, chitosan–chitosan, and water–IDP hydrogen bonding.</p>
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17 pages, 2941 KiB  
Article
Inhibition of Pro-Fibrotic Molecules Expression in Idiopathic Pulmonary Fibrosis—Derived Lung Fibroblasts by Lactose-Modified Hyaluronic Acid Compounds
by Alice Donato, Antonino Di Stefano, Nadia Freato, Laura Bertocchi and Paola Brun
Polymers 2024, 16(1), 138; https://doi.org/10.3390/polym16010138 - 31 Dec 2023
Cited by 2 | Viewed by 1495
Abstract
Idiopathic pulmonary fibrosis (IPF) is a chronic inflammatory and fibrotic pathological condition with undefined effective therapies and a poor prognosis, partly due to the lack of specific and effective therapies. Galectin 3 (Gal-3), a pro-fibrotic ß-galactoside binding lectin, was upregulated in the early [...] Read more.
Idiopathic pulmonary fibrosis (IPF) is a chronic inflammatory and fibrotic pathological condition with undefined effective therapies and a poor prognosis, partly due to the lack of specific and effective therapies. Galectin 3 (Gal-3), a pro-fibrotic ß-galactoside binding lectin, was upregulated in the early stages of the pathology, suggesting that it may be considered a marker of active fibrosis. In the present in vitro study, we use Hylach®, a lactose-modified hyaluronic acid able to bind Gal-3, to prevent the activation of lung myofibroblast and the consequent excessive ECM protein cell expression. Primary human pulmonary fibroblasts obtained from normal and IPF subjects activated with TGF-β were used, and changes in cell viability, fibrotic components, and pro-inflammatory mediator expression at both gene and protein levels were analyzed. Hylach compounds with a lactosylation degree of about 10% and 30% (Hylach1 and Hylach 2), administrated to TGF-β—stimulated lung fibroblast cultures, significantly downregulated α-smooth muscle actin (α-SMA) gene expression and decreased collagen type I, collagen type III, elastin, fibronectin gene and protein expression to near baseline values. This anti-fibrotic activity is accompanied by a strong anti-inflammatory effect and by a downregulation of the gene expression of Smad2 for both Hylachs in comparison to the native HA. In conclusion, the Gal-3 binding molecules Hylachs attenuated inflammation and TGF-β—induced over-expression of α-SMA and ECM protein expression by primary human lung fibroblasts, providing a new direction for the treatment of pulmonary fibrotic diseases. Full article
(This article belongs to the Special Issue Biopolymer for Biomedical Application)
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<p>Hylach<sup>®</sup> molecular structure.</p>
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<p>Expression of α-SMA and ECM molecules by lung fibroblast from healthy (<b>a</b>) and IPF donors (<b>b</b>) cultures exposed to 5 ng/mL TGF-β for 24 h. Quantification of RNA transcript levels was carried out using qPCR analyses. The data represent the mean ± standard error (SE) of results obtained from three independent experiments. Statistical differences were assessed using an unpaired Student’s <span class="html-italic">t</span>-test, and significance levels were indicated as follows: * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, and **** <span class="html-italic">p</span> &lt; 0.0001.</p>
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<p>Time-dependent impact of HA and Hylach on human lung fibroblast viability. 1200 cells from both healthy (<b>a</b>) and IPF (<b>b</b>) subjects were seeded in 96-well culture plates and treated with 0.5 mg/mL HA, Hylach 1, and Hylach 2 for 1, 3, and 6 days. Cell viability was measured using an MTT assay. Data are presented as the means ± standard error (SE) from three independent experiments. Statistical variances were assessed utilizing the unpaired Student’s <span class="html-italic">t</span>-test. The percentage of lactose derivative residues is as follows: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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<p>Modulation of α-Smooth Muscle Actin (α-SMA) gene expression in lung fibroblasts by Hylach and native HA. Human pulmonary fibroblasts from healthy (<b>a</b>) and IPF 8 (<b>b</b>) donors were exposed to TGF-β (5 ng/mL) for 24 h and subsequently cultured in the presence or absence of HA, Hylach 1, and Hylach 2. qPCR was employed to measure the mRNA level for α-SMA at 4, 10, and 24 h post-treatment. Statistical significance was determined via a one-way ANOVA test with multiple comparisons vs. untreated cells (* <span class="html-italic">p</span> &lt; 0.05, *** <span class="html-italic">p</span> &lt; 0.001, and **** <span class="html-italic">p</span> &lt; 0.0001). The results represent the mean ± standard error (SE) of three independent experiments. <span class="html-italic">Percentage of lactose derivative residues</span>: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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<p>ECM protein expression by TGF-β stimulated fibroblasts treated with HA and Hylach. Human pulmonary fibroblasts from control (<b>a</b>) and IPF (<b>b</b>) donors were exposed to TGF-β (5 ng/mL) for 24 h and then cultured in the presence or absence of HA, Hylach 1 or Hylach 2. mRNA levels for collagen I, collagen III, elastin, fibronectin, and TGF-β were analyzed using qPCR at 4, 10, and 24 h post-treatment. Statistical significance was determined via a one-way ANOVA test with multiple comparisons vs. untreated cells (* <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, and **** <span class="html-italic">p</span> &lt; 0.0001). The results represent the mean ± standard error (SE) of three independent experiments. <span class="html-italic">Percentage of lactose derivative residues</span>: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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<p>ECM protein expression by TGF-β stimulated fibroblasts treated with HA and Hylach. Human pulmonary fibroblasts from control (<b>a</b>) and IPF (<b>b</b>) donors were exposed to TGF-β (5 ng/mL) for 24 h and then cultured in the presence or absence of HA, Hylach 1 or Hylach 2. mRNA levels for collagen I, collagen III, elastin, fibronectin, and TGF-β were analyzed using qPCR at 4, 10, and 24 h post-treatment. Statistical significance was determined via a one-way ANOVA test with multiple comparisons vs. untreated cells (* <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, and **** <span class="html-italic">p</span> &lt; 0.0001). The results represent the mean ± standard error (SE) of three independent experiments. <span class="html-italic">Percentage of lactose derivative residues</span>: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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<p>Pro-inflammatory molecule gene expression in primary lung fibroblasts following exposure to U937 CM in the presence or absence of Hylach compounds and native HA. Primary human lung fibroblasts isolated from control and IPF donors were cultivated in the presence or absence of 0.5 mg/mL HA, Hylach 1, and Hylach 2 compounds after a 24 h exposure to activated U937 CM. At 4 and 10 h after the treatment, the gene expression of IL-1β, TNF-α, TGF-β, and Gal-3 was analyzed using qPCR. Statistical significance was determined via a one-way ANOVA test with multiple comparisons vs. untreated cells (* <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, and **** <span class="html-italic">p</span>&lt; 0.0001). The results represent the mean ± standard error (SE) of three independent experiments. Percentage of lactose derivative residues: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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<p><span class="html-italic">Smad-2</span> expression of primary human lung fibroblasts exposed to TGF-β in the presence or absence of Hylach and HA molecules. Cell cultures were exposed for 24 h to TGF-β and then cultured in the presence or absence of 0,5 mg/mL of Hylach or HA. RNA transcript levels for <span class="html-italic">Smad-2</span> were assessed using qPCR at 4, 10, and 24 h post-treatment. Statistical differences were determined using the ANOVA test with multiple comparisons vs. untreated cells (* <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01 and *** <span class="html-italic">p</span> &lt;0.001), and data are presented as mean ± SE obtained from three independent experiments. <span class="html-italic">Percentage of lactose derivative residues</span>: Hylach 1 = 10%, Hylach 2 = 30%.</p>
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16 pages, 3665 KiB  
Article
Development of an Innovative Lightweight Composite Material with Thermal Insulation Properties Based on Cardoon and Polyurethane
by Raquel A. Fernandes, Nuno Ferreira, Sandro Lopes, Jorge Santos, Nelson Bento Pereira, Nuno Oliveira Ferreira, Lina Nunes, Jorge M. Martins and Luisa H. Carvalho
Polymers 2024, 16(1), 137; https://doi.org/10.3390/polym16010137 - 31 Dec 2023
Viewed by 1479
Abstract
The search for innovative and sustainable solutions to improve the energy efficiency of the construction industry has been a hot topic for researchers due to the tremendous impact of insulator materials in the thermal comfort of buildings. In the present work, an innovative [...] Read more.
The search for innovative and sustainable solutions to improve the energy efficiency of the construction industry has been a hot topic for researchers due to the tremendous impact of insulator materials in the thermal comfort of buildings. In the present work, an innovative lightweight composite material with thermal insulation properties was developed, for the first time, by using cardoon particles and polyurethane. The formulation of the composite material was optimized in terms of cardoon fraction and the polyol/isocyanate ratio, to achieve the best compromise between internal bond (IB) strength and thickness swelling (TS). The best performing composite was PU75-CP45, with 45 wt% of cardoon particles and 75% of isocyanate, achieving an IB of 0.41 MPa and a TS of 5.3%. Regarding insulation properties, the PU75-CP45 composite material exhibits a promising performance when compared to conventional construction industry materials by tuning its thickness. Additionally, the composite material presented very low emissions of volatile organic compounds and formaldehyde (bellow to legislation levels) and high resistance to biological degradation. Full article
(This article belongs to the Special Issue Fibre-Reinforced Polymeric Composites)
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Figure 1
<p>(<b>a</b>) Photograph of the PUx-CPy composite panel. SEM micrographs of (<b>b</b>) cardoon particles (CP), (<b>c</b>) PU foam and (<b>d</b>) PUx-CPy composite panel. Dashed orange line and yellow arrows indicate regions of PU foam and CP aggregates, respectively.</p>
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<p>FTIR spectra of polyol (doted orange line), MDI (dashed green line) and PU (solid black line) foam. Blue zones and dashed blue line indicate specific FTIR bands.</p>
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<p>FTIR spectra of PU foam (black line), cardoon particles (blue line) and PUx-CPy composite material (red line). Yellow zones correspond to characteristic bands of transmittance.</p>
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<p>(<b>a</b>) TG curve and (<b>b</b>) TG first derivative of cardoon (doted blue line), PU foam (solid black line) and PUx-CPy composite material (dashed red line).</p>
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<p>Impact of cardoon content on the physical–mechanical performance of PU75-CPy composite materials: internal bond strength (IB, squares), thickness swelling (TS, triangles) and moisture content (MC, circles).</p>
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<p>Impact of MDI/polyol ratio on the mechanical performance of PUx-CP45 composite materials: internal bond strength (IB, squares), moisture content (MC, circles), and thickness swelling (TS, triangles).</p>
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<p>Thermal conductivity of PU75-CP45 composite material at 10 °C (open bars), 20 °C (dashed bars) and 30 °C (solid bars) with 250 (red bars) and 300 kg m<sup>−3</sup> (black bars) of density.</p>
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<p>Thermal resistance at 20 °C of PU75-CP45 and other materials (bars). Thickness (e) ratio of all materials, selecting rockwool (triangles) or EPS (circles) as standard material.</p>
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24 pages, 11647 KiB  
Article
Catalytic Ring-Opening Polymerisation of Cyclic Ethylene Carbonate: Importance of Elementary Steps for Determining Polymer Properties Revealed via DFT-MTD Simulations Validated Using Kinetic Measurements
by Daniel Brüggemann, Martin R. Machat, Reinhard Schomäcker and Mojgan Heshmat
Polymers 2024, 16(1), 136; https://doi.org/10.3390/polym16010136 - 31 Dec 2023
Cited by 1 | Viewed by 2039
Abstract
The production of CO2-containing polymers is still very demanding in terms of controlling the synthesis of products with pre-defined CO2 content and molecular weight. An elegant way of synthesising these polymers is via CO2-containing building blocks, such as [...] Read more.
The production of CO2-containing polymers is still very demanding in terms of controlling the synthesis of products with pre-defined CO2 content and molecular weight. An elegant way of synthesising these polymers is via CO2-containing building blocks, such as cyclic ethylene carbonate (cEC), via catalytic ring-opening polymerisation. However, to date, the mechanism of this reaction and control parameters have not been elucidated. In this work, using DFT-metadynamics simulations for exploiting the potential of the polymerisation process, we aim to shed more light on the mechanisms of the interaction between catalysts (in particular, the catalysts K3VO4, K3PO4, and Na2SnO3) and the cEC monomer in the propagation step of the polymeric chain and the occurring CO2 release. Confirming the simulation results via subsequent kinetics measurements indicates that, depending on the catalyst’s characteristics, it can be attached reversibly to the polymeric chain during polymerisation, resulting in a defined lifetime of the activated polymer chain. The second anionic oxygen of the catalyst can promote the catalyst’s transfer to another electrophilic cEC monomer, terminating the growth of the first chain and initiating the propagation of the new polymer chain. This transfer reaction is an essential step in controlling the molecular weight of the products. Full article
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Figure 1
<p>Example 3D spectrum of the in situ measurement of the reaction at 600RPM 140 °C.</p>
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<p>The considered mechanism of the ROP of cEC in a previous study. Step I, the proton abstraction by the catalyst anion and nucleophilic attack by the RO<sup>−</sup> to the carbonyl carbon of the cEC. Step II, the ring opening of the second cEC via the second nucleophilic attack by alkoxide and ring opening.</p>
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<p>The nucleophilic attack by the catalyst anion to the CH<sub>2</sub> of the cEC ring results in a terminal COO<sup>−</sup> and leads to the CO<sub>2</sub> release. CV1 and CV2 are the distances used for MTD simulation.</p>
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<p>Variation of the O<sup>−</sup>⋯C(CH<sub>2</sub>-O) distance (CV1) versus the C(H<sub>2</sub>)⋯O(ethereal) distance (CV2). Different regions can be identified based on the density of the dots (transient structures). The solid red bond shows the CH<sub>2</sub>-O(cEC) that is cleaved via nucleophilic attack by the catalyst anion and the dashed red line indicates the CH<sub>2</sub>-O(CAT) bond that is formed.</p>
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<p><b>Left</b>: various regions according to the density of the transient states in <a href="#polymers-16-00136-f004" class="html-fig">Figure 4</a>. <b>Right</b>: the schematic structures that correlate to the highlighted regions on the left side.</p>
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<p>The FESs of the CO<sub>2</sub> release mechanism and the energetics of the regions correspond to the areas depicted in <a href="#polymers-16-00136-f005" class="html-fig">Figure 5</a> for the three catalysts K<sub>3</sub>VO<sub>4</sub>, Na<sub>2</sub>SnO<sub>3</sub>, and K<sub>3</sub>PO<sub>4</sub> at 423 K. The energy values (numbers) are in kcal/mol. Two different patterns can be identified in the case of K<sub>3</sub>VO<sub>4</sub> and Na<sub>2</sub>SnO<sub>3</sub> (stepwise via an intermediate) versus K<sub>3</sub>PO<sub>4</sub> (concerted).</p>
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<p>Representative results of fitting the kinetic model to the experimental data. Experimental conditions: T<sub>R</sub> = 170 °C, c<sub>cEC</sub> = 13.83 mol/L, c<sub>Ethylenglycol</sub> = 1.38 mol/L, 0.01 eq. Potassium stannate. (<b>A</b>) Concentrate against the time of the reactants and products. (<b>B</b>) Fit the IR adsorption bands of the experiment to the experimental results.</p>
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<p><sup>31</sup>P NMR spectrum in CD<sub>2</sub>Cl<sub>2</sub> cEC polymer prepared with 0.02 eq. potassium phosphate as catalyst at reaction conditions: T<sub>R</sub> = 140 °C, RPM = 1000, experimental time = 5 h.</p>
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<p>The computationally considered pathway for chain growth starts from the catalyst–monomer molecular complex, while the catalyst is attached to the opened cEC.</p>
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<p>The computationally examined insertion paths starting from the attached CAT-cEC molecular complex, considering the second cEC as a nucleophile. The CO<sub>2</sub> release is the predominant possibility when the cEC is considered a nucleophile.</p>
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<p>(<b>A</b>) The observed pathway alongside the MTD simulation (instead of the CVs showed in <a href="#polymers-16-00136-f010" class="html-fig">Figure 10</a>); the second oxygen of the catalyst attacks the second cEC, and the chain propagation can also go via the second monomer. (<b>B</b>) The second observed path shows the catalyst detachment from the partially formed chain.</p>
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<p>The variation of the CVs and non-CV distances alongside the simulation of the insertion paths (<a href="#polymers-16-00136-f011" class="html-fig">Figure 11</a>). Variation of the non-CV distances triggered us to consider the new pathways of catalyst detachment and chain transfer, as shown in <a href="#polymers-16-00136-f013" class="html-fig">Figure 13</a>. CV2 is the CH<sub>2</sub>-O(ethereal) distance inside the cEC, which indicates the cEC cleavage.</p>
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<p><b>Upper part</b>: is the nucleophilic attack by the second O<sup>−</sup> of the catalyst anion to the second cEC, <b>lower part</b>: is the chain transfer and catalyst detachment path. The corresponding barriers for these trajectories are shown in <a href="#polymers-16-00136-t006" class="html-table">Table 6</a>.</p>
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<p>Plot of LC-ESI-MS spectra over time for monitoring the development of the molecular weight of the polymer using K<sub>2</sub>SnO<sub>3</sub> as the catalyst.</p>
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<p>Plot of LC-ESI-MS spectra over time for monitoring the development of the molecular weight of the polymer using K<sub>3</sub>PO<sub>4</sub> as the catalyst.</p>
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<p>Degree of polymerisation at different concentrations of catalyst. A significant reduction in the degree of polymerisation can be observed by increasing the catalyst concentration and thereby increasing the basicity. Tested system Starter: ethylene glycol (0.1 eq.) Catalyst: K<sub>2</sub>SnO<sub>3</sub> T: 150 °C.</p>
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<p><b>Left:</b> Arrhenius plots of the growth reactions for the incorporation and non-incorporation of CO<sub>2</sub> and the termination reaction (transfer) when using sodium orthovanadate (Na<sub>3</sub>VO<sub>4</sub>). The system used: catalyst (0.01 eq.), ethylene glycol (0.10 eq.), cyclic ethylene carbonate (1.00 eq.). <b>Right:</b> Arrhenius plot of the growth reactions for the incorporation and non-incorporation of CO<sub>2</sub> and the termination reaction (transfer) when using potassium stannate (K<sub>2</sub>SnO<sub>3</sub>). The system used: catalyst (0.01 eq.), ethylene glycol (0.10 eq.), cyclic ethylene carbonate (1.00 eq.).</p>
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<p>Catalytic ROP of cEC and exemplary molecular structure of the respective polyether carbonate polyol formed.</p>
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<p>The anionic ROP of cyclic carbonates (considered in this work).</p>
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<p>The considered molecular cluster for simulations; in this model cluster, there are six cEC molecules, one starter alcohol, and one typical catalyst molecule.</p>
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<p>The experimentally observed reaction network of cEC ROP, catalysed by SnO<sub>3</sub><sup>2−</sup> and VO<sub>4</sub><sup>3−</sup> anions. k<sub>1</sub>, k<sub>2</sub>, k<sub>3</sub>, and k<sub>4</sub> indicate the corresponding rate constants of ring-opening polymerisation (PECn), chain propagation with CO<sub>2</sub> release, decomposition of the chain, and CO<sub>2</sub> release from the chain, respectively.</p>
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<p>The experimentally observed reaction network was catalysed by PO<sub>4</sub><sup>3−</sup> anions. k<sub>1</sub>, k<sub>2</sub>, k<sub>3</sub>, and k<sub>4</sub> indicate the corresponding rate constants of polymerization, propagation with CO<sub>2</sub> release, decomposition of the chain, and CO<sub>2</sub> release from the chain, respectively. k<sub>des</sub> indicates the rate constant of catalyst deactivation.</p>
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<p>The previously proposed mechanism of cEC polymerisation, in which cEC attacks as a nucleophile to a second cEC [<a href="#B6-polymers-16-00136" class="html-bibr">6</a>].</p>
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