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Nanomaterials, Volume 11, Issue 1 (January 2021) – 254 articles

Cover Story (view full-size image): CO2 methanation has recently emerged as a process that converts captured CO2 and H2, produced from renewables, into CH4. Ni is currently being favoured as a catalytically active phase, but presents significant drawbacks, such as insufficient low‑temperature activity, low reducibility and nanoparticle sintering. Such problems can be partly overcome via the introduction of a second transition metal (e.g., Fe and Co) or a noble metal (e.g., Ru, Rh, Pt, Pd and Re) in Ni‑based catalysts. Through Ni–M alloy formation, or the intricate synergy between two adjacent metallic phases, new high-performing and low-cost methanation catalysts can be obtained. View this paper.
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11 pages, 3770 KiB  
Article
TiO2 Nanowires with Doped g-C3N4 Nanoparticles for Enhanced H2 Production and Photodegradation of Pollutants
by Liushan Jiang, Fanshan Zeng, Rong Zhong, Yu Xie, Jianli Wang, Hao Ye, Yun Ling, Ruobin Guo, Jinsheng Zhao, Shiqian Li and Yuying Hu
Nanomaterials 2021, 11(1), 254; https://doi.org/10.3390/nano11010254 - 19 Jan 2021
Cited by 6 | Viewed by 3985
Abstract
With the rapid consumption of fossil fuels, along with the ever-increasing environmental pollution, it is becoming a top priority to explore efficient photocatalysts for the production of renewable hydrogen and degradation of pollutants. Here, we fabricated a composite of g-C3N4 [...] Read more.
With the rapid consumption of fossil fuels, along with the ever-increasing environmental pollution, it is becoming a top priority to explore efficient photocatalysts for the production of renewable hydrogen and degradation of pollutants. Here, we fabricated a composite of g-C3N4/TiO2 via an in situ growth method under the conditions of high-temperature calcination. In this method, TiO2 nanowires with a large specific surface area could provide enough space for loading more g-C3N4 nanoparticles to obtain C3N4/TiO2 composites. Of note, the g-C3N4/TiO2 composite could effectively photocatalyze both the degradation of several pollutants and production of hydrogen, both of which are essential for environmental governance. Combining multiple characterizations and experiments, we found that the heterojunction constructed by the TiO2 and g-C3N4 could increase the photocatalytic ability of materials by prompting the separation of photogenerated carriers. Furthermore, the photocatalytic mechanism of the g-C3N4/TiO2 composite was also clarified in detail. Full article
(This article belongs to the Special Issue Application of Nanomaterials in Photocatalysis)
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Figure 1
<p>SEM images of TiO<sub>2</sub> (<b>a</b>,<b>b</b>) and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite (<b>c</b>).</p>
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<p>TEM images of TiO<sub>2</sub> (<b>a</b>) and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> (<b>b</b>); HRTEM images of TiO<sub>2</sub> (<b>c</b>) and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> (<b>d</b>).</p>
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<p>The XRD patterns of TiO<sub>2</sub>, g-C<sub>3</sub>N<sub>4</sub>, and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> samples with different mass ratios.</p>
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<p>The N<sub>2</sub> adsorption–desorption isothermal curve (<b>a</b>); pore diameter distribution curves (<b>b</b>).</p>
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<p>The high-resolution XPS spectra of the 40% g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite: survey (<b>a</b>), C 1s (<b>b</b>), O 1s (<b>c</b>), Ti 2p (<b>d</b>), and N 1s (<b>e</b>).</p>
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<p>The UV-vis diffuse reflectance spectra (<b>a</b>) and band gaps (<b>b</b>) of TiO<sub>2</sub> and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite.</p>
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<p>The photodegradation curves for methyl orange (<b>a</b>) and the photodegradation curves for rose red (<b>b</b>) with g-C<sub>3</sub>N<sub>4</sub>, TiO<sub>2</sub>, and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite; the methyl orange cycling photodegradation experiments with 40% g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite (<b>c</b>).</p>
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<p>Photocatalytic hydrogen production ability (<b>a</b>) and hydrogen production rate tests (<b>b</b>) of g-C<sub>3</sub>N<sub>4</sub>, TiO<sub>2</sub>, and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> samples.</p>
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<p>Photocurrent tests of TiO<sub>2</sub> and g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> samples with different mass ratios.</p>
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<p>Photocatalytic degradation by (<b>a</b>) and hydrogen production (<b>b</b>) mechanism of g-C<sub>3</sub>N<sub>4</sub>/TiO<sub>2</sub> composite.</p>
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17 pages, 4854 KiB  
Article
Assessment of the Influence of Crystalline Form on Cyto-Genotoxic and Inflammatory Effects Induced by TiO2 Nanoparticles on Human Bronchial and Alveolar Cells
by Anna Maria Fresegna, Cinzia Lucia Ursini, Aureliano Ciervo, Raffaele Maiello, Stefano Casciardi, Sergio Iavicoli and Delia Cavallo
Nanomaterials 2021, 11(1), 253; https://doi.org/10.3390/nano11010253 - 19 Jan 2021
Cited by 19 | Viewed by 3266
Abstract
Titanium dioxide nanoparticles (TiO2NPs) are increasingly used in consumer products, industrial and medical applications, raising concerns on their potential toxicity. The available in vitro and in vivo studies on these NPs show controversial results. Crystalline structure is the physicochemical characteristic that [...] Read more.
Titanium dioxide nanoparticles (TiO2NPs) are increasingly used in consumer products, industrial and medical applications, raising concerns on their potential toxicity. The available in vitro and in vivo studies on these NPs show controversial results. Crystalline structure is the physicochemical characteristic that seems to influence mainly TiO2NPs toxicity, so its effect needs to be further studied. We aimed to study whether and how crystalline form influences potential cyto-genotoxic and inflammatory effects induced by two commercial TiO2NPs (TiO2-A, mainly anatase; TiO2-B, mainly rutile) in human alveolar A549 and bronchial BEAS-2B cells exposed to 1–40 µg/mL. Cell viability (WST-1), membrane damage (LDH release), IL-6, IL-8 and TNF-α release (ELISA) and direct/oxidative DNA damage (fpg-comet assay) were evaluated. Physicochemical characterization included analysis of crystalline form (TEM and XRD), specific surface area (BET), agglomeration (DLS) and Z-potential (ELS). Our results show that TiO2-A NPs induce in BEAS-2B cytotoxicity and a slight inflammation and in A549 slight oxidative effects, whereas TiO2-B NPs induce genotoxic/oxidative effects in both cell lines, revealing different toxicity mechanisms for the two tested NPs. In conclusion, our study confirms the influence of crystalline form on cellular response, also demonstrating the suitability of our in vitro model to screen early TiO2NPs effects. Full article
(This article belongs to the Special Issue Advances in Toxicity of Nanoparticles)
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<p>(<b>a</b>) TEM micrographs of TiO<sub>2</sub>-A and (<b>b</b>) TiO<sub>2</sub>-B NPs dispersed in water and deposited on a 300-mesh Cu grid coated with carbon film (bar 50 nm). (<b>c</b>) XRD pattern of TiO<sub>2</sub>-A: anatase: 79% and φ ≈ 45 nm, rutile: 21% and φ ≈ 6 nm; (<b>d</b>) XRD pattern of TiO<sub>2</sub>-B: anatase: 19% and φ ≈ 87 nm, rutile: 81% and φ ≈ 75 nm. Panel (<b>c</b>) related to TiO<sub>2</sub>-A has been previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
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<p>TEM TiO<sub>2</sub>-B NPs characterization. (<b>a</b>) TEM micrograph of TiO<sub>2</sub>-B NPs dispersed in water and deposited on a 300-mesh Cu grid coated with carbon film (bar 50 nm); (<b>b</b>) HRTEM image which reveals lattice planes of the particles inside the box marked in panel (<b>a</b>); (<b>c</b>) the EELS spectrum of NPs shown in the inset shows the peaks of the Ti-L<sub>2,3</sub> thresholds (461 eV and 455 eV) and of the O-K threshold (532 eV); (<b>d</b>) Electron nanodiffraction pattern of the particle shown in the inset.</p>
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<p>Viability percentage of A549 (<b>a</b>) and BEAS-2B (<b>b</b>) cells after 24 h exposure to TiO<sub>2</sub>NPs evaluated by the WST-1 assay. * <span class="html-italic">p</span> ≤ 0.05, ** <span class="html-italic">p</span> &lt; 0.01. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
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<p>Lactate dehydrogenase (LDH) release expressed as a per cent of cytotoxicity in A549 and BEAS-2B cells after 30 min (<b>a</b>,<b>b</b>), 2 h (<b>c</b>,<b>d</b>) and 24 h (<b>e</b>,<b>f</b>) exposure to TiO<sub>2</sub>NPs. * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
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<p>Direct and oxidative DNA damage in A549 and BEAS-2B cells after 2 h (<b>a</b>,<b>b</b>,<b>e</b>,<b>f</b>) and 24 h (<b>c</b>,<b>d</b>,<b>g</b>,<b>h</b>) exposure to TiO<sub>2</sub>NPs evaluated by the Fpg-comet test. * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
Full article ">Figure 5 Cont.
<p>Direct and oxidative DNA damage in A549 and BEAS-2B cells after 2 h (<b>a</b>,<b>b</b>,<b>e</b>,<b>f</b>) and 24 h (<b>c</b>,<b>d</b>,<b>g</b>,<b>h</b>) exposure to TiO<sub>2</sub>NPs evaluated by the Fpg-comet test. * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
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<p>Cytokine release after 2 h (<b>a</b>,<b>b</b>,<b>e</b>,<b>f</b>) and 24 h (<b>c</b>,<b>d</b>,<b>g</b>,<b>h</b>) exposure to TiO<sub>2</sub>NPs in A549 and BEAS-2B cells. * <span class="html-italic">p</span> ≤ 0.05. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
Full article ">Figure 6 Cont.
<p>Cytokine release after 2 h (<b>a</b>,<b>b</b>,<b>e</b>,<b>f</b>) and 24 h (<b>c</b>,<b>d</b>,<b>g</b>,<b>h</b>) exposure to TiO<sub>2</sub>NPs in A549 and BEAS-2B cells. * <span class="html-italic">p</span> ≤ 0.05. Data relative to TiO<sub>2</sub>-A are previously published in [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>] (Reproduced with permission from [<a href="#B10-nanomaterials-11-00253" class="html-bibr">10</a>]. Copyright John Wiley &amp; Sons, Ltd., 2014).</p>
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62 pages, 11396 KiB  
Review
Electrochemical Sensors Based on Conducting Polymers for the Aqueous Detection of Biologically Relevant Molecules
by Álvaro Terán-Alcocer, Francisco Bravo-Plascencia, Carlos Cevallos-Morillo and Alex Palma-Cando
Nanomaterials 2021, 11(1), 252; https://doi.org/10.3390/nano11010252 - 19 Jan 2021
Cited by 62 | Viewed by 9245
Abstract
Electrochemical sensors appear as low-cost, rapid, easy to use, and in situ devices for determination of diverse analytes in a liquid solution. In that context, conducting polymers are much-explored sensor building materials because of their semiconductivity, structural versatility, multiple synthetic pathways, and stability [...] Read more.
Electrochemical sensors appear as low-cost, rapid, easy to use, and in situ devices for determination of diverse analytes in a liquid solution. In that context, conducting polymers are much-explored sensor building materials because of their semiconductivity, structural versatility, multiple synthetic pathways, and stability in environmental conditions. In this state-of-the-art review, synthetic processes, morphological characterization, and nanostructure formation are analyzed for relevant literature about electrochemical sensors based on conducting polymers for the determination of molecules that (i) have a fundamental role in the human body function regulation, and (ii) are considered as water emergent pollutants. Special focus is put on the different types of micro- and nanostructures generated for the polymer itself or the combination with different materials in a composite, and how the rough morphology of the conducting polymers based electrochemical sensors affect their limit of detection. Polypyrroles, polyanilines, and polythiophenes appear as the most recurrent conducting polymers for the construction of electrochemical sensors. These conducting polymers are usually built starting from bifunctional precursor monomers resulting in linear and branched polymer structures; however, opportunities for sensitivity enhancement in electrochemical sensors have been recently reported by using conjugated microporous polymers synthesized from multifunctional monomers. Full article
(This article belongs to the Special Issue Functional Nanomaterials for Sensor Applications)
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<p>Schematic representation of the molecularly imprinted polymers fabrication process of composite MIPs/ZNTs/FTO glass and its interaction with dopamine. Reproduced with permission from [<a href="#B90-nanomaterials-11-00252" class="html-bibr">90</a>]. Copyright 2017 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of composite polypyrrole (PPy)-Ag. Reproduced with permission from [<a href="#B93-nanomaterials-11-00252" class="html-bibr">93</a>]. Copyright 2020 Elsevier B.V.</p>
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<p>Schematic representation of different synthetic pathways for manufacturing the composite polyaniline-p-toluene sulphonic acids PANI-pTSA. Reproduced with permission from [<a href="#B98-nanomaterials-11-00252" class="html-bibr">98</a>]. Copyright 2019 Elsevier B.V.</p>
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<p>SEM images of (<b>a</b>) PANI, (<b>b</b>) poly-β-CD, and (<b>c</b>) poly-β-CD (f-MWCNTs)/PANI composite. Reproduced with permission from [<a href="#B99-nanomaterials-11-00252" class="html-bibr">99</a>]. Copyright 2019 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of PEDOT-Modified Laser Scribed Graphene (PEDOT-LSG) electrodes, and micrographs showing the morphology of LSG and PEDOT/LSG film. Modified with permission from [<a href="#B112-nanomaterials-11-00252" class="html-bibr">112</a>]. Copyright 2018 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of PEDOT/Au composites. Reproduced with permission from [<a href="#B114-nanomaterials-11-00252" class="html-bibr">114</a>]. Copyright 2017 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of PT/Au/CNT electrodes. Reproduced with permission from [<a href="#B120-nanomaterials-11-00252" class="html-bibr">120</a>]. Copyright 2019 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of pHQ/AuNPs over Ni Foam. Reproduced with permission from [<a href="#B125-nanomaterials-11-00252" class="html-bibr">125</a>]. Copyright 2017 Elsevier B.V.</p>
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<p>Schematic representation of the fabrication process of Au-PDNs (polydopamine nanospheres) electrodes. Reproduced with permission from [<a href="#B128-nanomaterials-11-00252" class="html-bibr">128</a>]. Copyright 2019 Elsevier B.V.</p>
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<p>SEM analysis of EB-PPy-BSA hybrid structure (<b>a</b>) micrograph, and (<b>b</b>) EDS spectrum. Modified with permission from [<a href="#B129-nanomaterials-11-00252" class="html-bibr">129</a>]. Copyright 2018 Elsevier B.V.</p>
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<p>SEM image of p(P3CA)/PGE surface in a magnification of (<b>a</b>) 10,000× and (<b>b</b>) 50,000×. Modified with permission from [<a href="#B137-nanomaterials-11-00252" class="html-bibr">137</a>]. Copyright 2015 Elsevier B.V.</p>
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<p>Schematic representation of the casting process of rGO−PEDOT/PSS-nafion composite onto gold mylar substrates. Reproduced with permission from [<a href="#B141-nanomaterials-11-00252" class="html-bibr">141</a>]. Copyright 2019 American Chemical Society.</p>
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<p>Schematic representation of the fabrication process of PEDOT/GO/ITO electrodes. Modified with permission from [<a href="#B148-nanomaterials-11-00252" class="html-bibr">148</a>]. Copyright 2019 Elsevier B.V.</p>
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<p>Micrograph of poly (6-thioguanine) film (P6-TG) deposited over glassy carbon electrode. Reproduced with permission from [<a href="#B152-nanomaterials-11-00252" class="html-bibr">152</a>]. Copyright 2015 Elsevier B.V.</p>
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<p>Scheme of EPI-4 structure used into a CPE to determinate AA. Yellow points represent gold nanoparticles. Reproduced with permission from [<a href="#B155-nanomaterials-11-00252" class="html-bibr">155</a>]. Copyright 2017 Elsevier.</p>
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<p>Schematic illustration for the preparation of duplex molecularly imprinted polymer/carbon paste electrodes (DMIP/CPE). Modified with permission from [<a href="#B207-nanomaterials-11-00252" class="html-bibr">207</a>]. Copyright 2016 Elsevier.</p>
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<p>Micrograph of molecularly imprinted polymers/golf nanoparticles/glassy carbon electrodes (MIP/AuNPs/GCE) microstructure (<b>a</b>) before and (<b>b</b>) after metronidazole extraction. Modified with permission from [<a href="#B208-nanomaterials-11-00252" class="html-bibr">208</a>]. Copyright 2015 Elsevier.</p>
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<p>FESEM images of (<b>a</b>) bare standard GCE, (<b>b</b>) nanoporous GCE, (<b>c</b>) PCC/nanoporous GCE and (<b>d</b>) CS-MWCNTs+TiO<sub>2</sub>NPs/PCC/nanoporous GCE. Reproduced with permission from [<a href="#B214-nanomaterials-11-00252" class="html-bibr">214</a>]. Copyright 2018 Electrochemical Society, Inc.</p>
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<p>FE-SEM micrographs of (<b>a</b>) CPE, (<b>b</b>) PEB/CPE and (<b>c</b>) SDS/PEB/CPE. Reproduced with permission from [<a href="#B218-nanomaterials-11-00252" class="html-bibr">218</a>]. Copyright 2019 Wiley-Blackwell Publishing Ltd.</p>
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<p>(<b>a</b>) EIS response of the MIP sensor towards 17-β-estradiol in the concentration of 1 aM to 10 μM. (<b>b</b>) Calibration curve of the R<sub>ct</sub> values versus the logarithm concentration of 17-β-estradiol. Modified with permission from [<a href="#B223-nanomaterials-11-00252" class="html-bibr">223</a>]. Copyright 2018 Elsevier.</p>
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<p>AFM images of the (<b>a</b>) unmodified glassy carbon electrode and (<b>b</b>) poly Nile blue modified glassy carbon electrode. Modified with permission from [<a href="#B231-nanomaterials-11-00252" class="html-bibr">231</a>]. Copyright 2016 Elsevier.</p>
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<p>SEM images of (<b>a</b>) Cu<sup>2+</sup>-PANI, (<b>b</b>) Cu<sup>2+</sup>-Nano-ZSM-5, and (<b>c</b>) Cu<sup>2+</sup>-PANI-Nano-ZSM-5 nanocomposite. Reproduced with permission from [<a href="#B237-nanomaterials-11-00252" class="html-bibr">237</a>]. Copyright 2015 Elsevier.</p>
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<p>CV responses of the FTO/PANI-gC<sub>3</sub>N<sub>4</sub>/AgNP electrode at a scan rate of 50 mV in the presence of different hydrazine concentrations. Modified with permission from [<a href="#B254-nanomaterials-11-00252" class="html-bibr">254</a>]. Copyright 2018 Elsevier.</p>
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<p>(<b>a</b>) Chronoamperogram for the sequential addition of catechol at Cu-PPy/GCE in 0.1 M PBS (pH = 7.0) at 0.3 V vs. SCE. (<b>b</b>) Schematic representation of the formation of a five-membered ring with Cu(II) and catechol and further oxidation of catechol at Cu-PPy/GCE. Modified with permission from [<a href="#B287-nanomaterials-11-00252" class="html-bibr">287</a>]. Copyright 2017 Electrochemical Society.</p>
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<p>Differential pulse voltammetry of poly (35DT)/Au electrode without 4-nitrophenol (solid square line), a bare gold electrode with 50 mM of 4-nitrophenol (solid circle line), and poly (35DT)/Au electrode with 50 μM of 4-nitrophenol (solid line). Modified with permission from [<a href="#B298-nanomaterials-11-00252" class="html-bibr">298</a>]. Copyright 2019 Wiley-VCH Verlag GmbbH and Co.</p>
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<p>FESEM images of polypyrrole/sodium dodecyl sulphate film, (<b>a</b>) before and (<b>b</b>) after electrochemical treatment. Modified with permission from [<a href="#B299-nanomaterials-11-00252" class="html-bibr">299</a>]. Copyright 2015 Elsevier.</p>
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14 pages, 5235 KiB  
Article
Magnetic and Electronic Properties of Weyl Semimetal Co2MnGa Thin Films
by Peter Swekis, Aleksandr S. Sukhanov, Yi-Cheng Chen, Andrei Gloskovskii, Gerhard H. Fecher, Ioannis Panagiotopoulos, Jörg Sichelschmidt, Victor Ukleev, Anton Devishvili, Alexei Vorobiev, Dmytro S. Inosov, Sebastian T. B. Goennenwein, Claudia Felser and Anastasios Markou
Nanomaterials 2021, 11(1), 251; https://doi.org/10.3390/nano11010251 - 19 Jan 2021
Cited by 27 | Viewed by 6611
Abstract
Magnetic Weyl semimetals are newly discovered quantum materials with the potential for use in spintronic applications. Of particular interest is the cubic Heusler compound Co2MnGa due to its inherent magnetic and topological properties. This work presents the structural, magnetic and electronic [...] Read more.
Magnetic Weyl semimetals are newly discovered quantum materials with the potential for use in spintronic applications. Of particular interest is the cubic Heusler compound Co2MnGa due to its inherent magnetic and topological properties. This work presents the structural, magnetic and electronic properties of magnetron co-sputtered Co2MnGa thin films, with thicknesses ranging from 10 to 80 nm. Polarized neutron reflectometry confirmed a uniform magnetization through the films. Hard x-ray photoelectron spectroscopy revealed a high degree of spin polarization and localized (itinerant) character of the Mn d (Co d) valence electrons and accompanying magnetic moments. Further, broadband and field orientation-dependent ferromagnetic resonance measurements indicated a relation between the thickness-dependent structural and magnetic properties. The increase of the tensile strain-induced tetragonal distortion in the thinner films was reflected in an increase of the cubic anisotropy term and a decrease of the perpendicular uniaxial term. The lattice distortion led to a reduction of the Gilbert damping parameter and the thickness-dependent film quality affected the inhomogeneous linewidth broadening. These experimental findings will enrich the understanding of the electronic and magnetic properties of magnetic Weyl semimetal thin films. Full article
(This article belongs to the Special Issue Synthesis, Development and Characterization of Magnetic Nanomaterials)
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Figure 1
<p>(<b>a</b>) XRD patterns of Co<sub>2</sub>MnGa films with different thicknesses. The inset shows the asymmetric 113 reflections. (<b>b</b>) Lattice parameters of Co<sub>2</sub>MnGa films as a function of thickness.</p>
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<p>(<b>a</b>–<b>d</b>) AFM topographic images of the Co<sub>2</sub>MnGa films with different thicknesses.</p>
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<p>(<b>a</b>) PNR measurements of an 80-nm-thick Co<sub>2</sub>MnGa film. The solid lines are the fitted curves. (<b>b</b>) Nuclear and magnetic SLD profiles obtained from fitting the PNR data. The right axis shows the magnetization corresponding to the magnetic SLD profile.</p>
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<p>(<b>a</b>) Co 2<span class="html-italic">p</span> and (<b>b</b>) Mn 2<span class="html-italic">p</span> HAXPES spectra of Co<sub>2</sub>MnGa film on MgO(001). Shown are spectra taken with <span class="html-italic">σ</span><sup>+</sup> and <span class="html-italic">σ</span><sup>−</sup> polarization of the photons. The insets show the difference spectra, that is the dichroism.</p>
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<p>Magnetization hysteresis loops with <span class="html-italic">H</span> applied along the: (<b>a</b>) IP and (<b>b</b>) OOP film directions at 300 K for Co<sub>2</sub>MnGa films of various thicknesses.</p>
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<p>(<b>a</b>–<b>d</b>) Resonance fields <span class="html-italic">µ</span><sub>0</sub><span class="html-italic">H</span><sub>res</sub> with <span class="html-italic">H</span> applied perpendicular to the film plane for the Co<sub>2</sub>MnGa films with various thicknesses; and (<b>e</b>–<b>h</b>) linewidths of the respective FMR modes, including linear fits for the damping parameters.</p>
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<p>Resonance fields <span class="html-italic">H</span><sub>res</sub> and simulated resonance conditions (solid lines, see main text) at 300 K and 9.4 GHz of Co<sub>2</sub>MnGa films with different thicknesses: (<b>a</b>–<b>d</b>) <span class="html-italic">H</span> rotated in the (001) plane, i.e., IP rotation; and (<b>e</b>–<b>h</b>) <span class="html-italic">H</span> rotated in the (110) plane, i.e., IP to OOP rotation. The dashed lines indicate the crystallographic directions of the film at the respective angles. Inset in (<b>h</b>): Cartesian and polar coordinate system, where the crystallographic directions refer to the Co<sub>2</sub>MnGa film and the angles to the direction of <span class="html-italic">H</span>.</p>
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16 pages, 1792 KiB  
Article
In Vitro Interactions of TiO2 Nanoparticles with Earthworm Coelomocytes: Immunotoxicity Assessment
by Natividad Isabel Navarro Pacheco, Radka Roubalova, Jaroslav Semerad, Alena Grasserova, Oldrich Benada, Olga Kofronova, Tomas Cajthaml, Jiri Dvorak, Martin Bilej and Petra Prochazkova
Nanomaterials 2021, 11(1), 250; https://doi.org/10.3390/nano11010250 - 19 Jan 2021
Cited by 10 | Viewed by 4100
Abstract
Titanium dioxide nanoparticles (TiO2 NPs) are manufactured worldwide. Once they arrive in the soil environment, they can endanger living organisms. Hence, monitoring and assessing the effects of these nanoparticles is required. We focus on the Eisenia andrei earthworm immune cells exposed to [...] Read more.
Titanium dioxide nanoparticles (TiO2 NPs) are manufactured worldwide. Once they arrive in the soil environment, they can endanger living organisms. Hence, monitoring and assessing the effects of these nanoparticles is required. We focus on the Eisenia andrei earthworm immune cells exposed to sublethal concentrations of TiO2 NPs (1, 10, and 100 µg/mL) for 2, 6, and 24 h. TiO2 NPs at all concentrations did not affect cell viability. Further, TiO2 NPs did not cause changes in reactive oxygen species (ROS) production, malondialdehyde (MDA) production, and phagocytic activity. Similarly, they did not elicit DNA damage. Overall, we did not detect any toxic effects of TiO2 NPs at the cellular level. At the gene expression level, slight changes were detected. Metallothionein, fetidin/lysenin, lumbricin and MEK kinase I were upregulated in coelomocytes after exposure to 10 µg/mL TiO2 NPs for 6 h. Antioxidant enzyme expression was similar in exposed and control cells. TiO2 NPs were detected on coelomocyte membranes. However, our results do not show any strong effects of these nanoparticles on coelomocytes at both the cellular and molecular levels. Full article
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<p>Transmission electron microscopy of 500 µg/mL TiO<sub>2</sub> NPs clustered in distilled water. The scale bar represents 200 nm.</p>
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<p>Scanning electron microscopy of coelomocytes. (<b>A</b>) cells exposed to 100 μg/mL TiO<sub>2</sub> NPs for 2 h; (<b>B</b>) control cells cultured in the medium. Images recorded with B + C segments of a CBS detector at 3 kV. White arrow indicates a TiO<sub>2</sub> NPs cluster on sample support. Clusters of the same morphology can be seen on the cell surface (white double arrow). The scale bar represents 5 μm.</p>
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<p>EDS microanalysis of coelomocytes incubated with 100 µg/mL TiO<sub>2</sub> NPs. (<b>A</b>) An image showing the area of interest taken with EDX TEAM software at 15 kV using a SED detector. The spectra collection places are marked with EDS labels. Increased charging effects caused by the non-conductive nature of Thermanox coverslips used for sample preparation deteriorated image quality. (<b>B</b>) EDS microanalysis confirmed Ti in NPs clusters found on the cell surface (e.g., EDS Spot 2 label) and also in the cluster labeled EDS spot 1. Blue arrow indicates TiO<sub>2</sub> NPs cluster (EDS Spot 2 label), green arrow points to the cell surface without NPs clusters (EDS Spot 4 label). Corresponding EDS spectra in matching colors are shown in B. The scale bar represents 5 µm.</p>
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<p>ROS production by hyaline (HA) and granular (GA). ROS production was measured in HA and GA after incubation with 1, 10, and 100 µg/mL TiO<sub>2</sub> NPs for 2, 6, and 24 h using a cell-permeant tracer 2′,7′-dichlorofluorescein diacetate (DCF-DA). Coelomocytes were also exposed to 1 mM H<sub>2</sub>O<sub>2</sub> (positive control) for 30 min. The results are shown as the mean of fluorescence intensity (DCF-DA) ± SEM of three independent experiments with 3 replicates in each. *** <span class="html-italic">p</span> &lt; 0.001, and * <span class="html-italic">p</span> &lt; 0.05 according to two-way ANOVA and Bonferroni post-test.</p>
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<p>Early and late apoptosis, viability and necrosis of hyaline amoebocytes (HA). Early and late apoptosis, viability and necrosis of HA of non-treated cells, cells exposed to 1, 10, and 100 µg/mL TiO<sub>2</sub> NPs after 2, 6, and 24 h. 10 mM H<sub>2</sub>O<sub>2</sub> was used as positive control for 30 min exposure. The results are shown as mean (%) ± SEM of three independent experiments with 3 replicates in each. *** <span class="html-italic">p</span> &lt; 0.001, and ** <span class="html-italic">p</span> &lt; 0.01 according to two-way ANOVA and Bonferroni post-test.</p>
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<p>Early and late apoptosis, viability and necrosis of granular amoebocytes (GA). Early and Late apoptosis, viability and necrosis of GA of non-treated cells, cells exposed to 1, 10, and 100 µg/mL TiO<sub>2</sub> NPs after 2, 6, and 24 h. 10 mM H<sub>2</sub>O<sub>2</sub> was used as positive control for 30 min exposure. The results are shown as mean (%) ± SEM of three independent experiments with 3 replicates in each. ** <span class="html-italic">p</span> &lt; 0.01, and * <span class="html-italic">p</span> &lt; 0.05 according to two-way ANOVA and Bonferroni post-test.</p>
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<p>Phagocytic activity of HA and GA. Phagocytic activity was measured after incubation with TiO<sub>2</sub> NPs (1, 10, and 100 µg/mL) for 2, 6, and 24 h. Coelomocytes were also exposed to 10 mM H<sub>2</sub>O<sub>2</sub> (positive control) for 30 min. Results are represented as the mean ± SEM of three independent experiments with 3 replicates in each. *** <span class="html-italic">p</span> &lt; 0.001, ** <span class="html-italic">p</span> &lt; 0.01, and * <span class="html-italic">p</span> &lt; 0.05 according to two-way ANOVA and Bonferroni post-test.</p>
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<p>Relative malondialdehyde (MDA) production in coelomocytes exposed to 10, 100 µg/mL TiO<sub>2</sub> NPs and positive control (100 µg/mL CuSO<sub>4</sub>) for 2, 6, and 24 h. Values are expressed as mean (%) ± SEM of three independent experiments each with three replicates. *** <span class="html-italic">p</span> &lt; 0.001 according to two-way ANOVA and Bonferroni post-test.</p>
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<p>DNA damage in coelomocytes after their exposure to 1, 10, and 100 µg/mL TiO<sub>2</sub> NPs for 2, 6, and 24 h. Coelomocytes were also exposed to 100 mM H<sub>2</sub>O<sub>2</sub> (positive control) for 30 min. Values are expressed as the mean of DNA content in tail (%) ± SEM of three experiment with three replicates. *** <span class="html-italic">p</span> &lt; 0.001 and * <span class="html-italic">p</span> &lt; 0.05 according to two-way ANOVA and Bonferroni post-test.</p>
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18 pages, 5591 KiB  
Article
Conformation of Polyethylene Glycol inside Confined Space: Simulation and Experimental Approaches
by Tianji Ma, Nicolas Arroyo, Jean Marc Janot, Fabien Picaud and Sebastien Balme
Nanomaterials 2021, 11(1), 244; https://doi.org/10.3390/nano11010244 - 19 Jan 2021
Cited by 8 | Viewed by 3217
Abstract
The modification of the inner nanopore wall by polymers is currently used to change the specific properties of the nanosystem. Among them, the polyethylene glycol (PEG) is the most used to prevent the fouling and ensure the wettability. However, its properties depend mainly [...] Read more.
The modification of the inner nanopore wall by polymers is currently used to change the specific properties of the nanosystem. Among them, the polyethylene glycol (PEG) is the most used to prevent the fouling and ensure the wettability. However, its properties depend mainly on the chain structure that is very difficult to estimate inside this confined space. Combining experimental and simulation approaches, we provide an insight to the consequence of the PEG presence inside the nanopore on the nanopore properties. We show, in particular, that the cation type in the electrolyte, together with the type of electrolyte (water or urea), is at the origin of the ion transport modification in the nanopore. Full article
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<p>On the left and upper right, respectively, a profile and a front view of the starting point of simulations. On the lower right is shown the front view of the KCl system without urea after 20 ns of simulation. Only PEG (polyethylene glycol) and the pore are represented here.</p>
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<p>Conductance as a function of KCl concentration for (<b>a</b>) conical nanopore (<span class="html-italic">d<sub>tip</sub></span> = 10 nm, <span class="html-italic">D<sub>base</sub></span> = 200 nm) and (<b>b</b>) cylindrical nanopore (<span class="html-italic">d</span> = 19 nm) before (black square) and after (red, circle) PEG functionalization. (<b>c</b>) Evolution of cover rate of PEG calculated from the decrease of conductance at low salt concentration for cylindrical nanopores.</p>
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<p>Conductance as a function of KCl concentration for (<b>a</b>) conical nanopore (<span class="html-italic">d<sub>tip</sub></span> = 10 nm, <span class="html-italic">D<sub>base</sub></span> = 200 nm) and (<b>b</b>) cylindrical nanopore (<span class="html-italic">d</span> = 19 nm) before (black square) and after (red, circle) PEG functionalization. (<b>c</b>) Evolution of cover rate of PEG calculated from the decrease of conductance at low salt concentration for cylindrical nanopores.</p>
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<p>IV curves obtained for the small conical nanopore (<span class="html-italic">d<sub>tip</sub></span> = 10 nm, <span class="html-italic">D<sub>base</sub></span> = 200 nm) under LiCl (<b>a</b>) and KCl (<b>b</b>) solution; (<b>c</b>) Nanopore conductance as a function of KCl and LiCl concentration, the dash line are the linear fits at high salt concentration to measure the nanopore diameter; (<b>d</b>) Map depicting the measure PEG layer thickness for small nanopore (square) and large nanopore (circle); the dash line are the expected value obtained from Flory’s law and Equation (4) assuming a maximum surface density of 0.33 PEG nm<sup>−</sup>².</p>
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<p>IV curves obtained for the small conical nanopore (<span class="html-italic">d<sub>tip</sub></span> = 10 nm, <span class="html-italic">D<sub>base</sub></span> = 200 nm) under LiCl (<b>a</b>) and KCl (<b>b</b>) solution; (<b>c</b>) Nanopore conductance as a function of KCl and LiCl concentration, the dash line are the linear fits at high salt concentration to measure the nanopore diameter; (<b>d</b>) Map depicting the measure PEG layer thickness for small nanopore (square) and large nanopore (circle); the dash line are the expected value obtained from Flory’s law and Equation (4) assuming a maximum surface density of 0.33 PEG nm<sup>−</sup>².</p>
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<p>Radial distributions of every component inside the tube after 25 ns of simulation averaged from the last 5 ns. Cations (either K<sup>+</sup> or Li<sup>+</sup>) are shown in red and Cl<sup>−</sup> in blue. PEGs are shown in green. Water is represented in purple, its density in the graph is divided by 10 to improve clarity. KCl solvent is shown on the left graph while LiCl is shown on the right.</p>
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<p>Current under 1 V and −1 V recorded under LiCl (<b>a</b>) and KCl (<b>b</b>) solution; (<b>c</b>) Evolution of ionic current rectification as a function of electrolyte concentration.</p>
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<p>IV curves obtained for the small conical nanopore (d<span class="html-italic"><sub>tip</sub></span> = 10 nm, D<span class="html-italic"><sub>base</sub></span> = 200 nm) under KCl 1 M (<b>a</b>) and 0.01 M (<b>b</b>) and LiCl 1 M (<b>d</b>) and 0.01 M (<b>e</b>) solution (different colors have been chosen as a function of the urea concentration as shown in the inset caption); Nanopore conductance as a function of urea concentration KCl and LiCl 1 M (<b>c</b>) and 0.01 M (<b>f</b>); (<b>g</b>) Evolution of ionic current rectification as a function of urea concentration.</p>
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<p>IV curves obtained for the small conical nanopore (d<span class="html-italic"><sub>tip</sub></span> = 10 nm, D<span class="html-italic"><sub>base</sub></span> = 200 nm) under KCl 1 M (<b>a</b>) and 0.01 M (<b>b</b>) and LiCl 1 M (<b>d</b>) and 0.01 M (<b>e</b>) solution (different colors have been chosen as a function of the urea concentration as shown in the inset caption); Nanopore conductance as a function of urea concentration KCl and LiCl 1 M (<b>c</b>) and 0.01 M (<b>f</b>); (<b>g</b>) Evolution of ionic current rectification as a function of urea concentration.</p>
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<p>IV curves obtained for the small conical nanopore (d<span class="html-italic"><sub>tip</sub></span> = 10 nm, D<span class="html-italic"><sub>base</sub></span> = 200 nm) under KCl 1 M (<b>a</b>) and 0.01 M (<b>b</b>) and LiCl 1 M (<b>d</b>) and 0.01 M (<b>e</b>) solution (different colors have been chosen as a function of the urea concentration as shown in the inset caption); Nanopore conductance as a function of urea concentration KCl and LiCl 1 M (<b>c</b>) and 0.01 M (<b>f</b>); (<b>g</b>) Evolution of ionic current rectification as a function of urea concentration.</p>
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<p>Radial distributions of every component inside the tube after 40 ns of simulation averaged from the last 5 ns. Cations (either K<sup>+</sup> or Li<sup>+</sup>) are shown in red and Cl<sup>−</sup> in blue. PEGs are shown in green. Water is represented in purple, its density in the graph is divided by 10 to improve clarity; urea is shown in orange. KCl solvent with urea is on the left graph while LiCl with urea is on the right.</p>
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<p>Pair interaction energy in kcal/mol between both water and urea and the nanopore surface (not including graphene sheets) over the duration of the simulation. We see how urea/surface energy decreases (i.e., attraction increases) while water/surface energy increases.</p>
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<p>RMSD of PEG structures from the beginning of simulations without (<b>left</b>) and with (<b>right</b>) urea. Systems with KCl are shown in red while LiCl is in blue.</p>
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<p>Front view visualization of the KCl systems, without (<b>left</b>) and with (<b>right</b>) urea after, respectively, 25 and 40 ns of simulated time. PEG, water and urea near the pore surface are shown in green, purple and orange, respectively. Nanopore is shown in teal and red.</p>
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13 pages, 1750 KiB  
Article
Mechanical Properties and Bioactivity of Poly(Lactic Acid) Composites Containing Poly(Glycolic Acid) Fiber and Hydroxyapatite Particles
by Han-Seung Ko, Sangwoon Lee, Doyoung Lee and Jae Young Jho
Nanomaterials 2021, 11(1), 249; https://doi.org/10.3390/nano11010249 - 18 Jan 2021
Cited by 43 | Viewed by 4008
Abstract
To enhance the mechanical strength and bioactivity of poly(lactic acid) (PLA) to the level that can be used as a material for spinal implants, poly(glycolic acid) (PGA) fibers and hydroxyapatite (HA) were introduced as fillers to PLA composites. To improve the poor interface [...] Read more.
To enhance the mechanical strength and bioactivity of poly(lactic acid) (PLA) to the level that can be used as a material for spinal implants, poly(glycolic acid) (PGA) fibers and hydroxyapatite (HA) were introduced as fillers to PLA composites. To improve the poor interface between HA and PLA, HA was grafted by PLA to form HA-g-PLA through coupling reactions, and mixed with PLA. The size of the HA particles in the PLA matrix was observed to be reduced from several micrometers to sub-micrometer by grafting PLA onto HA. The tensile and flexural strength of PLA/HA-g-PLA composites were increased compared with those of PLA/HA, apparently due to the better dispersion of HA and stronger interfacial adhesion between the HA and PLA matrix. We also examined the effects of the length and frequency of grafted PLA chains on the tensile strength of the composites. By the addition of unidirectionally aligned PGA fibers, the flexural strength of the composites was greatly improved to a level comparable with human compact bone. In the bioactivity tests, the growth of apatite on the surface was fastest and most uniform in the PLA/PGA fiber/HA-g-PLA composite. Full article
(This article belongs to the Section Nanocomposite Materials)
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<p>(<b>a</b>) FT-IR, (<b>b</b>,<b>c</b>) XPS for N1s, and (<b>d</b>) TGA of surface-grafted hydroxyapatite (HA): (<b>b</b>) HA-Hexamethylene diisocyanate (HMDI); (<b>c</b>) HA-HMDI-ethylene glycol (EG).</p>
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<p>SEM images of fracture surface of (<b>a</b>) PLA/HA5, (<b>b</b>) PLA/HA10, (<b>c</b>) PLA/HA15, (<b>d</b>) PLA/HA-g-PLA(m)5, (<b>e</b>) PLA/HA-g-PLA(m)10, (<b>f</b>) PLA/HA-g-PLA(m)15, (<b>g</b>) PLA/PGA fiber10, (<b>h</b>) PLA/PGA fiber20, and (<b>i</b>) PLA/PGA fiber30.</p>
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<p>(<b>a</b>) Flexural stress–strain curves, (<b>b</b>) flexural modulus, and (<b>c</b>) flexural strength of PLA and its composites: PLA (black solid line); PLA/PGA fiber30 (black dash line); PLA/PGA fiber30/HA10 (gray solid line); PLA/PGA fiber30/HA-g-PLA(m)10 (gray dash line).</p>
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<p>(<b>a</b>) Weight loss by phosphate buffer saline (PBS) and (<b>b</b>) weight increase by simulated body fluid (SBF) solution of the composites: ■ PLA/PGA fiber30; ● PLA/PGA fiber30/HA10; ▲ PLA/PGA fiber30/HA-g-PLA(m)10.</p>
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<p>Surface SEM images of the composites before and after apatite growth by immersing PLA/PGA fiber30 (<b>A</b>), PLA/PGA fiber30/HA10 (<b>B</b>), and PLA/PGA fiber30/HA-g-PLA(m)10 (<b>C</b>) in SBF solution. The subscript number represents the immersing days of the composites.</p>
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10 pages, 2439 KiB  
Article
Reduction of the Diazo Functionality of ?-Diazocarbonyl Compounds into a Methylene Group by NH3BH3 or NaBH4 Catalyzed by Au Nanoparticles
by Marios Kidonakis and Manolis Stratakis
Nanomaterials 2021, 11(1), 248; https://doi.org/10.3390/nano11010248 - 18 Jan 2021
Cited by 3 | Viewed by 2980
Abstract
Supported Au nanoparticles on TiO2 (1 mol%) are capable of catalyzing the reduction of the carbene-like diazo functionality of α-diazocarbonyl compounds into a methylene group [C=(N2) → CH2] by NH3BH3 or NaBH4 in methanol [...] Read more.
Supported Au nanoparticles on TiO2 (1 mol%) are capable of catalyzing the reduction of the carbene-like diazo functionality of α-diazocarbonyl compounds into a methylene group [C=(N2) → CH2] by NH3BH3 or NaBH4 in methanol as solvent. The Au-catalyzed reduction that occurs within a few minutes at room temperature formally requires one hydride equivalent (B-H) and one proton that originates from the protic solvent. This pathway is in contrast to the Pt/CeO2-catalyzed reaction of α-diazocarbonyl compounds with NH3BH3 in methanol, which leads to the corresponding hydrazones instead. Under our stoichiometric Au-catalyzed reaction conditions, the ketone-type carbonyls remain intact, which is in contrast to the uncatalyzed conditions where they are selectively reduced by the boron hydride reagent. It is proposed that the transformation occurs via the formation of chemisorbed carbenes on Au nanoparticles, having proximally activated the boron hydride reagent. This protocol is the first general example of catalytic transfer hydrogenation of the carbene-like α -ketodiazo functionality. Full article
(This article belongs to the Special Issue Nano Au Materials for Catalysis of Organic Transformations)
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<p>Reduction of α-diazocarbonyl compounds by NH<sub>3</sub>BH<sub>3</sub> or NaBH<sub>4</sub> catalyzed by Au/TiO<sub>2</sub>. <sup>a</sup> With one additional B-H equivalent, the corresponding alcohols of the ketones <b>3j</b>–<b>l</b> were isolated in &gt;90% yield. <sup>b</sup> In this case, the corresponding hydrazone (Ε/Ζ = 85/15) was formed in 15% relative yield using NH<sub>3</sub>BH<sub>3</sub> and in 25% with NaBH<sub>4</sub>. The isolated yield refers to the reaction with NH<sub>3</sub>BH<sub>3</sub>.</p>
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<p>Hydrosilylation of α-diazo carbonyl compounds catalyzed by Au/TiO<sub>2</sub>; reversal of chemoselectivity of the attempted hydrosilylation of diazo compound <b>1a</b> in the presence of 0.5 equivalents of H<sub>2</sub>O.</p>
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<p>Reduction of α-diazocarbonyl compound <b>1a</b> by boron hydride reagents in methanol catalyzed by Au/TiO<sub>2</sub>, and D-labeling experiments in the reduction of compound <b>1b</b>.</p>
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<p>The reaction of α-diazocarbonyl compounds with NH<sub>3</sub>BH<sub>3</sub> in methanol under different catalytic conditions.</p>
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<p>Au/TiO<sub>2</sub>-catalyzed reaction of <b>1a</b> with excess of NaBH<sub>4</sub> or NH<sub>3</sub>BH<sub>3</sub>, and a proof that hydrazones are not reaction intermediates.</p>
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<p>Mechanistic considerations in the reduction of α-diazocarbonyl compounds with NH<sub>3</sub>BH<sub>3</sub> catalyzed by Au/TiO<sub>2</sub> (the catalytic sites of nanoparticles are indicated as Au<sub>n</sub>).</p>
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16 pages, 6842 KiB  
Article
Cellulose Nanocrystals and Corn Zein Oxygen and Water Vapor Barrier Biocomposite Films
by Tal Ben Shalom, Shylee Belsey, Michael Chasnitsky and Oded Shoseyov
Nanomaterials 2021, 11(1), 247; https://doi.org/10.3390/nano11010247 - 18 Jan 2021
Cited by 26 | Viewed by 4243
Abstract
Cellulose nanocrystals (CNC) are well-suited to the preparation of biocomposite films and packaging material due to its abundance, renewability, biodegradability, and favorable film-forming capacity. In this study, different CNC and corn zein (CZ) composite films were prepared by adding CZ to the CNC [...] Read more.
Cellulose nanocrystals (CNC) are well-suited to the preparation of biocomposite films and packaging material due to its abundance, renewability, biodegradability, and favorable film-forming capacity. In this study, different CNC and corn zein (CZ) composite films were prepared by adding CZ to the CNC suspension prior to drying, in order to change internal structure of resulting films. Films were developed to examine their performance as an alternative water vapor and oxygen-barrier for flexible packaging industry. Water vapor permeability (WVP) and oxygen transmission rate (OTR) of the biocomposite films decreased significantly in a specific ratio between CNC and CZ combined with 1,2,3,4-butane tetracarboxylic acid (BTCA), a nontoxic cross linker. In addition to the improved barrier properties, the incorporation of CZ benefitted the flexibility and thermal stability of the CNC/CZ composite films. The toughness increased by 358%, and Young’s modulus decreased by 32% compared with the pristine CNC film. The maximum degradation temperature increased by 26 °C, compared with that of CNC film. These results can be attributed to the incorporation of a hydrophobic protein into the matrix creating hydrophobic interactions among the biocomposite components. SEM and AFM analysis indicated that CZ could significantly affect the CNC arrangement, and the film surface topography, due to the mechanical bundling and physical adsorption effect of CZ to CNC. The presented results indicate that CNC/CZ biocomposite films may find applications in packaging, and in multi-functionalization materials. Full article
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<p>Solubility of CZ protein in ethanol /water mixture.</p>
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<p>Suspension stability. (<b>a</b>) Flocculation of CZ in DW, (<b>b</b>) CNC/CZ improved suspension stability.</p>
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<p>Transparency of CNC, crosslinked CNC films, and nanocomposite CNC/CZ films with different CZ contents. (<b>a</b>) Non crosslinked films, (<b>b</b>) crosslinked films.</p>
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<p>Water absorption over time. (<b>a</b>) non-crosslinked CNC and nanocomposite CNC/CZ films and (<b>b</b>) crosslinked nanocomposite CNC/CZ films.</p>
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<p>WVP of nanocomposite CNC/CZ film as affected by different CZ concentration and crosslinking.</p>
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<p>Films water contact angle as affected by different CNC/CZ ratio and crosslinking.</p>
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<p>Comparative OTR of various films samples. All samples are coated on a 30 µm corona treated biaxially-oriented polypropylene (BOPP) film.</p>
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<p>SEM images of non-cross linked CNC and CNC/CZ films. The images are at a magnification of 23,000×.</p>
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<p>SEM images of cross linked CNC and CNC/CZ films. The images are at a magnification of 23,000×.</p>
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<p>Effect of CZ content on surface roughness of CNC nanocomposite films. (<b>a</b>) Non-cross linked films (<b>b</b>) cross linked films.</p>
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<p>Tensile testing of crosslinked and non-crosslinked CNC films, nanocomposite CNC\CZ films (<b>a</b>) Tensile stress at break, (<b>b</b>) tensile strain at break, (<b>c</b>) Young’s modulus and (<b>d</b>) toughness.</p>
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<p>TGA curves of CNC and CNC/CZ films. (<b>a</b>) Non-cross linked films (<b>b</b>) cross linked films.</p>
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33 pages, 8793 KiB  
Review
Recent Advance in the Fabrication of 2D and 3D Metal Carbides-Based Nanomaterials for Energy and Environmental Applications
by Keming Wan, Yalin Li, Yan Wang and Gang Wei
Nanomaterials 2021, 11(1), 246; https://doi.org/10.3390/nano11010246 - 18 Jan 2021
Cited by 48 | Viewed by 5841
Abstract
Two-dimensional (2D) nanomaterials have attracted increased interest and exhibited extended applications from nanotechnology to materials science, biomedicine, tissue engineering, as well as energy storage and environmental science. With the development of the synthesis and fabrication of 2D materials, a new family of 2D [...] Read more.
Two-dimensional (2D) nanomaterials have attracted increased interest and exhibited extended applications from nanotechnology to materials science, biomedicine, tissue engineering, as well as energy storage and environmental science. With the development of the synthesis and fabrication of 2D materials, a new family of 2D materials, metal carbides (MCs), revealed promising applications in recent years, and have been utilized for the fabrication of various functional 2D and three-dimensional (3D) nanomaterials for energy and environmental applications, ascribing to the unique physical and chemical properties of MCs. In this review, we present recent advance in the synthesis, fabrication, and applications of 2D and 3D MC-based nanomaterials. For this aim, we first summarize typical synthesis methods of MCs, and then demonstrate the progress on the fabrication of 2D and 3D MC-based nanomaterials. To the end, the applications of MC-based 2D and 3D materials for chemical batteries, supercapacitors, water splitting, photodegradation, removal of heavy metals, and electromagnetic shielding are introduced and discussed. This work provides useful information on the preparation, hybridization, structural tailoring, and applications of MC-based materials, and is expected to inspire the design and fabrication of novel and functional MXene materials with improved performance. Full article
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<p>(<b>a</b>) The etching process of MAX phase and the formation of MXene. Reproduced from [<a href="#B38-nanomaterials-11-00246" class="html-bibr">38</a>], with permission from, American Chemistry Society, 2012. (<b>b</b>) Schematic of MS-Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> MXene preparation process. Reproduced from [<a href="#B39-nanomaterials-11-00246" class="html-bibr">39</a>], with permission from Nature Publishing Group, 2020. (<b>c</b>) Electrochemical method of Ti<sub>3</sub>C<sub>2</sub> stratification in binary water electrolyte. Reproduced from [<a href="#B40-nanomaterials-11-00246" class="html-bibr">40</a>], with permission from Wiley, 2018. (<b>d</b>) The preparation of Ti<sub>3</sub>AlC<sub>2</sub> using different temperatures and concentrations of sodium hydroxide, where higher temperatures and alkali concentrations help dissolve Al, and push the entire etching process to the production of MXene. Reproduced from [<a href="#B41-nanomaterials-11-00246" class="html-bibr">41</a>], with permission from Wiley, 2018.</p>
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<p>(<b>a</b>) Schematic of the M-CMP synthesis program. (<b>b</b>) Area electron diffraction pattern of M-CMP nanosheet. M-CMP still preserves an apparent relatively obvious sheet structure, indicating that the reaction did not cause serious accumulation and thus destroy the structure of MXene. (<b>c</b>) High resolution TEM (HRTEM) image of M-CMP’s microporous structure. The light and dark parts are alternately displayed, which can explain the micropore structure with uniform pore distribution in M-CMP. Reproduced from [<a href="#B57-nanomaterials-11-00246" class="html-bibr">57</a>], with permission from Wiley, 2020. (<b>d</b>) The synthesis method and formation mechanism of Ni@MXene heterides. (<b>e</b>) TEM image of Ni@MXene hybrid, in which Ni nanoparticles are uniformly attached to the Ti3C2Tx nanosheets. Reproduced from [<a href="#B58-nanomaterials-11-00246" class="html-bibr">58</a>], with permission from American Chemical Society, 2019. (<b>f</b>) Schematic diagram of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/CNT complex synthesized by CVD. Reproduced from [<a href="#B59-nanomaterials-11-00246" class="html-bibr">59</a>], with permission from Royal Society of Chemistry, 2017. (<b>g</b>) Mechanism of GO/MXene composite membrane in water purification process. (<b>h</b>) SEM images on the surface of GO/MXene composite film with mass ratio of 1/1. Reproduced from [<a href="#B60-nanomaterials-11-00246" class="html-bibr">60</a>], with permission from Elsevier, 2019.</p>
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<p>(<b>a</b>) Schematic illustration of the LbL self-assembly of (MXene/TAEA)<sub>n</sub> multilayer films onto planar substratesa. Reproduced from [<a href="#B65-nanomaterials-11-00246" class="html-bibr">65</a>], with permission from Nature Publishing Group, 2019. (<b>b</b>,<b>c</b>) The morphology and microstructure of MXM: freeze-drying (<b>b</b>) and capillary-drying (<b>c</b>). (<b>d</b>) MXene-based Hydrogel synthesis diagram. Reproduced from [<a href="#B66-nanomaterials-11-00246" class="html-bibr">66</a>], with permission from Wiley, 2019. (<b>e</b>) A schematic illustrating the fabrication process and digital images showing the light weight of the MXene/PI aerogel, which can rest on the top of a dandelion. (<b>f</b>) The SEM image of MXene/PI aerogel, which has a compact interface and an interconnected porous structure. Reproduced from [<a href="#B67-nanomaterials-11-00246" class="html-bibr">67</a>], with permission from Wiley, 2018.</p>
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<p>Schematic of MXene clay synthesis and electrode preparation: (<b>a</b>) the schematic of MXene clay synthesis and electrode preparation processes. (<b>b</b>) When the dried sample (left) is hydrated (right), it will expand. (<b>c</b>) The produced flexible, free-standing film in a roller mill between water-permeable membranes. (<b>d</b>) Mold “clay” into the letter M and dry it to obtain a conductive solid. Reproduced from [<a href="#B42-nanomaterials-11-00246" class="html-bibr">42</a>], with permission from Nature Publishing Group, 2014. (<b>e</b>) The intercalation of ions in layered compounds has been used for a long time in energy storage devices such as batteries and electrochemical capacitors. Reproduced from [<a href="#B72-nanomaterials-11-00246" class="html-bibr">72</a>], with permission from Royal Society of Chemistry, 2019.</p>
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<p>Schematic illustration showing the synthesis of CoF NP-decorated MXene and its application as a supercapacitor electrode. Reproduced from [<a href="#B76-nanomaterials-11-00246" class="html-bibr">76</a>], with permission from American Chemical Society, 2020.</p>
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<p>Schematic diagram of the relationship between carrier mobility and direction of 2D Zr<sub>2</sub>CO<sub>2</sub> and Hf<sub>2</sub>CO<sub>2</sub> and the separation of photogenerated electron-hole pairs. Reproduced from [<a href="#B81-nanomaterials-11-00246" class="html-bibr">81</a>], with permission from Royal Society of Chemistry, 2016.</p>
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<p>Degradation mechanism of pollutants by photocatalyst prepared with MXene: (<b>a</b>) Schematic mechanism of magnetic α-Fe<sub>2</sub>O<sub>3</sub>/ZnFe<sub>2</sub>O<sub>4</sub>@Ti<sub>3</sub>C<sub>2</sub> MXene photocatalyst. Reproduced from [<a href="#B85-nanomaterials-11-00246" class="html-bibr">85</a>], with permission from Elsevier, 2020. (<b>b</b>) Schematic diagram for the decomposition of organic pollutants under visible light irradiation. Reproduced from [<a href="#B87-nanomaterials-11-00246" class="html-bibr">87</a>], with permission from Elsevier, 2019.</p>
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<p>Adsorption performance of MX-SA<sub>4:20</sub> in a multi-component system: (<b>a</b>) Diagram showing that Hg<sup>2 +</sup> ions are absorbed by MX-SA<sub>4:20</sub> spheres. (<b>b</b>) The batch system simultaneously adsorbs eight toxic metal ions. (<b>c</b>) Breakthrough curve in fixed adsorption of multi-ions. Reproduced from [<a href="#B97-nanomaterials-11-00246" class="html-bibr">97</a>], with permission from Elsevier, 2019.</p>
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<p>(<b>a</b>) EMI SE versus thickness of different materials. (<b>b</b>) EMI shielding mechanism. The incoming EM wave (green arrow) hits the surface of the MXene sheet. Due to the large number of charge carriers on the highly conductive surface, part of the electromagnetic wave was immediately reflected from the surface (light blue arrow), and the induced local dipole generated by the end base helps to absorb the incident wave through the MXene structure (blue dotted line). The transmitted wave changes when it encounters the next MXene sheet, causing multiple internal reflections (black dashed line) and more absorption. Reproduced from [<a href="#B103-nanomaterials-11-00246" class="html-bibr">103</a>], with permission from AAAS, 2016.</p>
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<p>Fabrication, structures and applications of various metal carbides-based nanomaterials.</p>
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17 pages, 10561 KiB  
Article
Modification of Surface Bond Au Nanospheres by Chemically and Plasmonically Induced Pd Deposition
by Heike Lisa Kerstin Stephanie Stolle, Andrea Csáki, Jan Dellith and Wolfgang Fritzsche
Nanomaterials 2021, 11(1), 245; https://doi.org/10.3390/nano11010245 - 18 Jan 2021
Cited by 2 | Viewed by 2781
Abstract
In this work we investigated methods of modifying gold nanospheres bound to a silicon surface by depositing palladium onto the surfaces of single nanoparticles. Bimetallic Au-Pd nanoparticles can thus be gained for use in catalysis or sensor technology. For Pd deposition, two methods [...] Read more.
In this work we investigated methods of modifying gold nanospheres bound to a silicon surface by depositing palladium onto the surfaces of single nanoparticles. Bimetallic Au-Pd nanoparticles can thus be gained for use in catalysis or sensor technology. For Pd deposition, two methods were chosen. The first method was the reduction of palladium acetate by ascorbic acid, in which the amounts of palladium acetate and ascorbic acid were varied. In the second method we utilized light-induced metal deposition by making use of the plasmonic effect. Through this method, the surface bond nanoparticles were irradiated with light of wavelengths capable of inducing plasmon resonance. The generation of hot electrons on the particle surface then reduced the palladium acetate in the vicinity of the gold nanoparticle, resulting in palladium-covered gold nanospheres. In our studies we demonstrated the effect of both enhancement methods by monitoring the particle heights over enhancement time by atomic force microscopy (AFM), and investigated the influence of ascorbic acid/Pd acetate concentration as well as the impact of the irradiated wavelengths on the enhancement effect. It could thus be proven that both methods were valid for obtaining a deposition of Pd on the surface of the gold nanoparticles. Deposition of Pd on the gold particles using the light-assisted method could be observed, indicating the impact of the plasmonic effect and hot electron for Pd acetate reduction on the gold particle surface. In the case of the reduction method with ascorbic acid, in addition to Pd deposition on the gold nanoparticle surface, larger pure Pd particles and extended clusters were also generated. The reduction with ascorbic acid however led to a considerably thicker Pd layer of up to 54 nm in comparison to up to 11 nm for the light-induced metal deposition with light resonant to the particle absorption wavelength. Likewise, it could be demonstrated that light of non-resonant wavelengths was not capable of initiating Pd deposition, since a growth of only 1.6 nm (maximum) was observed for the Pd layer. Full article
(This article belongs to the Section Synthesis, Interfaces and Nanostructures)
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<p>Formation mechanism of AuPd nanoparticles (AuPdNP) from Au nanoparticles (AuNP) by reduction of Pd acetate with ascorbic acid to Pd<sup>0</sup>, dehydroascorbic acid, and acetic acid.</p>
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<p>Atomic force microscopy (AFM) images of 80-nm gold nanospheres (AuNPs) after 0 min (<b>a</b>), 4 min (<b>b</b>), and 10 min (<b>c</b>) of enhancement with 1.5 mM palladium acetate (PdAc) and 228 mM ascorbic acid. Insets: Height profiles of the marked nanoparticle (<b>a</b>, red arrow) over time. The scale bar of image 1a pertains to all three images.</p>
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<p>SEM images of the chip with 228 mM AS and 1.5 mM PdAc after a total enhancement time of 10 min. (<b>a</b>) Agglomerates and newly formed Pd particles besides AuPd particles. (<b>b</b>) Close-up of AuPd particles.</p>
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<p>Development of particle weight during experiments with (<b>a</b>) a constant Pd acetate concentration of 2.5 mM and (<b>b</b>) a constant ascorbic acid concentration of 228 mM.</p>
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<p>Formation mechanism of AuPd nanoparticles (AuPdNP) by light-induced reduction of Pd acetate by hot electrons generated through the irradiation of the Au nanoparticles (AuNP) with light of resonant wavelengths.</p>
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<p>UV/Vis spectra of 30 and 80 nm Au NPs (<b>top</b>) and spectra of utilized light sources (<b>bottom</b>).</p>
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<p>(<b>a</b>–<b>c</b>) AFM images of Pd enhancement of 80-nm AuNPs with white light and (<b>d</b>–<b>f</b>) of 30-nm AuNPs with green light with captures of 0, 4, and 10 min, respectively. Insets: Height profiles of the marked particle (red arrow) over time. The scale bar of image 6a also pertains to images b and c and the scale bar of image 6d also pertains to images e and f.</p>
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<p>SEM images after irradiation of AuNPs in PdAc solution: (<b>a</b>) 80-nm AuNPs (white light) and (<b>b</b>) 30-nm AuNPs (green light). Insets show a close up of the respective particles.</p>
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<p>(<b>a</b>) Development of particle height after each enhancement step of two minutes for 80-nm AuNPs and white light and (<b>b</b>) for 30-nm AuNPs with green light.</p>
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<p>Development of particle height in experiments with different light sources with 80 and 30 nm AuNPs for 10 min.</p>
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<p>Energy-dispersive X-ray spectrometry (EDX) line analysis of an exemplary AuPd nanoparticle (inset, chip with 80-nm AuNPs and 114-mM AS, 2.5-mM PdAc).</p>
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<p>EDX line analysis of an exemplary AuPd nanoparticle (inset, chip with 80-nm AuNPs and 2.5-mM PdAc and step-wise irradiation with white light).</p>
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9 pages, 1308 KiB  
Communication
Quantification of Nitric Oxide Concentration Using Single-Walled Carbon Nanotube Sensors
by Jakob Meier, Joseph Stapleton, Eric Hofferber, Abigail Haworth, Stephen Kachman and Nicole M. Iverson
Nanomaterials 2021, 11(1), 243; https://doi.org/10.3390/nano11010243 - 18 Jan 2021
Cited by 26 | Viewed by 3816
Abstract
Nitric oxide (NO), a free radical present in biological systems, can have many detrimental effects on the body, from inflammation to cancer. Due to NO’s short half-life, detection and quantification is difficult. The inability to quantify NO has hindered researchers’ understanding of its [...] Read more.
Nitric oxide (NO), a free radical present in biological systems, can have many detrimental effects on the body, from inflammation to cancer. Due to NO’s short half-life, detection and quantification is difficult. The inability to quantify NO has hindered researchers’ understanding of its impact in healthy and diseased conditions. Single-walled carbon nanotubes (SWNTs), when wrapped in a specific single-stranded DNA chain, becomes selective to NO, creating a fluorescence sensor. Unfortunately, the correlation between NO concentration and the SWNT’s fluorescence intensity has been difficult to determine due to an inability to immobilize the sensor without altering its properties. Through the use of a recently developed sensor platform, systematic studies can now be conducted to determine the correlation between SWNT fluorescence and NO concentration. This paper explains the methods used to determine the equations that can be used to convert SWNT fluorescence into NO concentration. Through the use of the equations developed in this paper, an easy method for NO quantification is provided. The methods outlined in this paper will also enable researchers to develop equations to determine the concentration of other reactive species through the use of SWNT sensors. Full article
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<p>Schematic of testing process. (<b>A</b>) Sensor-coated slide was placed into a heated slide holder and then bathed in saline (25 °C). The slide/slide holder was placed on the upright microscope and imaged before and after the addition of various NO concentrations. With the addition of increasing concentrations of NO, there is a decrease in the fluorescent signal emitted by the SWNT. (<b>B</b>) A schematic showing the change in fluorescence emission with the addition of NO.</p>
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<p>Fluorescence quenching curves. (<b>A</b>) An example quenching curve before and after the addition of 10 µM NO. (<b>B</b>) Signal intensity over time, forming quenching curves that display the average response of the SWNT sensors to different concentrations of NO.</p>
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<p>Difference in signal intensity for different NO concentrations. (<b>A</b>) The change in fluorescence intensity of the SWNT compared to NO concentration, with individual data points in red and averaged data points in black and (<b>B</b>) concentration curve (<span class="html-italic">x</span> = (<span class="html-italic">y</span> − 28.59)/3.73, with <span class="html-italic">x</span> = NO concentration in µM and <span class="html-italic">y</span> = difference in fluorescence intensity) that can be used to convert SWNT fluorescence changes into NO concentration. <span class="html-italic">R</span><sup>2</sup> value = 0.99.</p>
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<p>Slope of signal intensity after the addition of different concentrations of NO. (<b>A</b>) The slope of the fluorescence intensity of the SWNT compared to NO concentration, with individual data points in blue and averaged data points in black and (<b>B</b>) concentration curve (<span class="html-italic">x</span> = −(<span class="html-italic">y</span> + 0.21)/0.42, with <span class="html-italic">x</span> = NO concentration in µM and <span class="html-italic">y</span> = slope of signal intensity) that can be used to convert SWNT fluorescence changes into NO concentration. <span class="html-italic">R</span><sup>2</sup> value = 0.99.</p>
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15 pages, 4297 KiB  
Article
High-Performance Humidity Sensor Based on the Graphene Flower/Zinc Oxide Composite
by Muhammad Saqib, Shenawar Ali Khan, Hafiz Mohammad Mutee Ur Rehman, Yunsook Yang, Seongwan Kim, Muhammad Muqeet Rehman and Woo Young Kim
Nanomaterials 2021, 11(1), 242; https://doi.org/10.3390/nano11010242 - 18 Jan 2021
Cited by 36 | Viewed by 4527
Abstract
Performance of an electronic device relies heavily on the availability of a suitable functional material. One of the simple, easy, and cost-effective ways to obtain novel functional materials with improved properties for desired applications is to make composites of selected materials. In this [...] Read more.
Performance of an electronic device relies heavily on the availability of a suitable functional material. One of the simple, easy, and cost-effective ways to obtain novel functional materials with improved properties for desired applications is to make composites of selected materials. In this work, a novel composite of transparent n-type zinc oxide (ZnO) with a wide bandgap and a unique structure of graphene in the form of a graphene flower (GrF) is synthesized and used as the functional layer of a humidity sensor. The (GrF/ZnO) composite was synthesized by a simple sol–gel method. Morphological, elemental, and structural characterizations of GrF/ZnO composite were performed by a field emission scanning electron microscope (FESEM), energy-dispersive spectroscopy (EDS), and an x-ray diffractometer (XRD), respectively, to fully understand the properties of this newly synthesized functional material. The proposed humidity sensor was tested in the relative humidity (RH) range of 15% RH% to 86% RH%. The demonstrated sensor illustrated a highly sensitive response to humidity with an average current change of 7.77 μA/RH%. Other prominent characteristics shown by this device include but were not limited to high stability, repeatable results, fast response, and quick recovery time. The proposed humidity sensor was highly sensitive to human breathing, thus making it a promising candidate for various applications related to health monitoring. Full article
(This article belongs to the Special Issue Nanomaterials and Devices)
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<p>Process flow diagram: (<b>a</b>) substrate cleaning (<b>b</b>) electrode printing (<b>c</b>) UV-ozone treatment (<b>d</b>) sol–gel ZnO thin film deposition (<b>e</b>) graphene flower (GrF) spray coating (<b>f</b>) annealing for 1 h.</p>
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<p>Experimental setup used for electrical measurement of the device under test (DUT).</p>
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<p>Characterization of graphene flowers, (<b>a</b>–<b>c</b>) field emission scanning electron microscope (FESEM) analysis, (<b>d</b>) Raman analysis.</p>
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<p>FESEM analysis of grown thin films, (<b>a</b>–<b>c</b>) SEM images of ZnO thin film at different magnifications; (<b>d</b>–<b>f</b>) GrF/ZnO composite SEM images at various magnifications.</p>
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<p>EDS analysis of, (<b>a</b>) EDS spectrum of fluorine tin oxide (FTO) glass (that was used as a substrate); (<b>b</b>) EDS spectrum of ZnO thin film; (<b>c</b>) GrF/ZnO composite.</p>
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<p>XRD analysis of (<b>a</b>) ZnO thin film; (<b>b</b>) GrF/ZnO composite.</p>
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<p>Electrical response with respect to RH%, (<b>a</b>) current vs. RH%; (<b>b</b>) repeatability analysis and comparison of current at different RH% (inset shows the current comparison for low humidity levels); (<b>c</b>) current response of the GrF–ZnO composite-based sensor under switching RH; (<b>d</b>) sensitivity of GrF–ZnO sensor.</p>
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<p>Current vs. voltage at different RH%, (<b>a</b>) 15% RH; (<b>b</b>) 60% RH, (<b>c</b>) 72% RH and (<b>d</b>) 86% RH.</p>
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<p>(<b>a</b>) Response and recovery time; (<b>b</b>) stability test of the proposed sensor, (<b>c</b>) sensor response to normal human breathing.</p>
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24 pages, 5782 KiB  
Review
Construction of Inorganic Bulks through Coalescence of Particle Precursors
by Zhao Mu, Ruikang Tang and Zhaoming Liu
Nanomaterials 2021, 11(1), 241; https://doi.org/10.3390/nano11010241 - 18 Jan 2021
Cited by 12 | Viewed by 4178
Abstract
Bulk inorganic materials play important roles in human society, and their construction is commonly achieved by the coalescence of inorganic nano- or micro-sized particles. Understanding the coalescence process promotes the elimination of particle interfaces, leading to continuous bulk phases with improved functions. In [...] Read more.
Bulk inorganic materials play important roles in human society, and their construction is commonly achieved by the coalescence of inorganic nano- or micro-sized particles. Understanding the coalescence process promotes the elimination of particle interfaces, leading to continuous bulk phases with improved functions. In this review, we mainly focus on the coalescence of ceramic and metal materials for bulk construction. The basic knowledge of coalescent mechanism on inorganic materials is briefly introduced. Then, the properties of the inorganic precursors, which determine the coalescent behaviors of inorganic phases, are discussed from the views of particle interface, size, crystallinity, and orientation. The relationships between fundamental discoveries and industrial applications are emphasized. Based upon the understandings, the applications of inorganic bulk materials produced by the coalescence of their particle precursors are further presented. In conclusion, the challenges of particle coalescence for bulk material construction are presented, and the connection between recent fundamental findings and industrial applications is highlighted, aiming to provide an insightful outlook for the future development of functional inorganic materials. Full article
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<p>(<b>a</b>) Scheme of a single crystal structure, in which the atoms are in a repeating position, and the atomic bonds are linked between atoms. (<b>b</b>) Scheme of a free surface of a single crystal, showing disrupted atomic bonds. These dangling atomic bonds induce the surface energy; (<b>c</b>) scheme of two misoriented nanoparticles and the illustration of the misorientation angle; and (<b>d</b>) grain boundary energy changes with misorientation angle [<a href="#B25-nanomaterials-11-00241" class="html-bibr">25</a>].</p>
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<p>(<b>a</b>) Scheme for the protocol of the rapid sintering process; (<b>b</b>) the temperature profile of the ultrafast high-temperature sintering (UHS) process; (<b>c</b>) comparison of Li loss of different sintered Li<sub>6.5</sub>La<sub>3</sub>Zr<sub>1.5</sub>Ta<sub>0.5</sub>O<sub>12</sub> (LLZTO) samples (0, 10, and 20% excess Li) using the UHS technique and conventional furnaces; (<b>d</b>) scheme of high-throughput screening: co-sintering ~100 matrix with ~10 s; (<b>e</b>) schematics and energy dispersive spectroscopy mapping of the co-sintered Li<sub>1.3</sub>Al<sub>0.3</sub>Ti<sub>1.7</sub>(PO<sub>4</sub>)<sub>3</sub> (LATP)-LLZTO bilayer SSE; (<b>f</b>) a multilayer 3D-printed SiOC polymer precursor and a corresponding UHS-sintered sample; and (<b>g</b>) snapshots of the SiOC polymer precursor and SiOC samples sintered by the UHS method. Reproduced with permission [<a href="#B45-nanomaterials-11-00241" class="html-bibr">45</a>]. Copyright 2020, AAAS. RT, room temperature.</p>
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<p>(<b>a</b>) Scheme of the cold sintering from particle precursors. Molecular structures at the grain boundary have been magnified. Reproduced with permission [<a href="#B46-nanomaterials-11-00241" class="html-bibr">46</a>]. Copyright 2016, Wiley-VCH. (<b>b</b>) Scheme of cold co-sintered ceramic-polymer composites. (<b>c</b>,<b>d</b>) Scanning electron microscope (SEM) image of 90LM–10PTFE (<b>c</b>) and 40LM–60PTFE (<b>d</b>) composites, which are cold co-sintered at 120 °C and 350 MPa for 20 min. The white region is the Li<sub>2</sub>MoO<sub>4</sub> <sub>(</sub>LM) phase, while the black region is PTFE phase. Reproduced with permission [<a href="#B54-nanomaterials-11-00241" class="html-bibr">54</a>]. Copyright 2016, Wiley-VCH. (<b>e</b>) Capacitor arrays on Nickel foils by printing (1) or cold sintering (2). (<b>f</b>) SEM image on cross-sectional view of a cold-sintered Li<sub>2</sub>MoO<sub>4</sub>, showing a single-layered capacitor structure: (1) cold-sintered structure on polyethylene terephthalate film at low-magnification and (2) top and bottom electrodes in high-magnification image. Reproduced with permission [<a href="#B52-nanomaterials-11-00241" class="html-bibr">52</a>]. Copyright 2016, The American Ceramic Society.</p>
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<p>(<b>a</b>) Simulated structures of two solid nanoparticles during coalescence. Left column: two 6 nm nanoparticles; right column: two 2 nm nanoparticles. (<b>b</b>) The evolution of R<sub>d</sub> diameters at 2000 K for solid-solid coalescence model. (<b>c</b>) The evolution of temperature T during solidsolid coalescence process. Reproduced with permission [<a href="#B64-nanomaterials-11-00241" class="html-bibr">64</a>]. Copyright 2017, Elsevier B.V.</p>
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<p>(<b>a</b>) Scheme of the capping strategy and reaction conditions for producing (CaCO<sub>3</sub>)<sub>n</sub> oligomers; a photograph of gel-like (CaCO<sub>3</sub>)<sub>n</sub> oligomers is presented on the right. (<b>b</b>) Pair–distance distribution function (P(r)) of the (CaCO<sub>3</sub>)<sub>n</sub> oligomers. The shape simulation of the oligomer is shown in the inset. Error bars represent one standard deviation, n = 20. (<b>c</b>) high-resolution transmission electron microscope (HRTEM) images of (CaCO<sub>3</sub>)<sub>n</sub> oligomers grown at different Ca/triethylamine (TEA) ratios from 1:100 to 1:2. (<b>d</b>) Molded CaCO<sub>3</sub> with different dimensions and morphologies. (<b>e</b>) Schemes for pattern construction on single-crystalline calcite (top path), and the repair of rough single-crystalline calcite to smooth calcite (bottom path). The insets show optical microscopy images of the calcite surface at different stages: native, corroded, and repaired. Reproduced with permission [<a href="#B76-nanomaterials-11-00241" class="html-bibr">76</a>]. Copyright 2019, Springer Nature.</p>
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<p>(<b>a</b>) SEM image of Emiliania huxleyi (Skeffington and Scheffel, 2018). (<b>b</b>) SEM of small spine. Reproduced with permission [<a href="#B81-nanomaterials-11-00241" class="html-bibr">81</a>]. Copyright 2018, American Chemical Society. (<b>c</b>) HRTEM micrograph of a selected surface area of the single crystalline aragonite nacre platelets. Reproduced with permission [<a href="#B84-nanomaterials-11-00241" class="html-bibr">84</a>]. Copyright 2005, National Academy of Science. (<b>d</b>) Component mapping in 48 h spicules, at the prism developmental stage, analyzed within 24 h of extraction from the embryo. X-ray absorption near-edge structure spectroscopy and photoelectron emission microscopy (XANES-PEEM) image of three spicules embedded in epoxy. (<b>e</b>) Red, green, and blue (RGB) map displaying the results of component mapping. The box indicates the region magnified in f. (<b>f</b>) Zoomed-in portion of the RGB map in (<b>e</b>), where each 15 nm pixel shows a different color. Pure phases are R, G, or B, whereas mixed phases are cyan, magenta, or yellow. (<b>g</b>) Sequence of 20 XANES spectra extracted from 15 nm adjacent pixels along the white line in (<b>f</b>). The color-coding is the same as that used in (<b>e</b>,<b>f</b>). Notice that the white line in f runs from the outer rim of the spicule (red), passing through orange, yellow, green, cyan, and finally blue, toward the crystalline center of the spicule. Correspondingly, moving from bottom to top across the spectra in (<b>g</b>), one can see peak-2 growth leading, and peak-4 emergence and growth lagging. Reproduced with permission [<a href="#B85-nanomaterials-11-00241" class="html-bibr">85</a>]. Copyright 2012, National Academy of Science. (<b>h</b>) Attachment of nanocrystals onto the vaterite surface at early stages. Reproduced with permission [<a href="#B30-nanomaterials-11-00241" class="html-bibr">30</a>]. Copyright 2016, Wiley-VCH.</p>
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<p>(<b>a</b>–<b>g</b>) Sequence of images showing typical dynamics of the oriented attachment (OA) process. (<b>h</b>) High-resolution image of interface in (<b>g</b>) showing twin structure (an inclined twin plane). The yellow dashed line in (<b>g</b>) shows the original boundary of the attached particle. (<b>i</b>,<b>j</b>) High-resolution in situ TEM image (<b>i</b>) and fast Fourier transform (FFT) (<b>j</b>) of an interface. The grain boundary is delineated by a dashed line in (<b>i</b>). Scale bars are 5 nm for (a) to (<b>g</b>). Reproduced with permission [<a href="#B94-nanomaterials-11-00241" class="html-bibr">94</a>]. Copyright 2012, AAAS. (<b>k</b>) A small particle is attached to a bigger one without matching orientation. (<b>l</b>) Two particles have sintered together by building a boundary with a twin structure. (<b>m</b>) Two orientation matched particles have sintered together; the former shape is preserved. Reproduced with permission [<a href="#B86-nanomaterials-11-00241" class="html-bibr">86</a>]. Copyright 2008, American Physical Society. (<b>n</b>) Atomistic simulation for a two-particle geometry, where two particles are rotated by an equal, but opposite angle, <span class="html-italic">θ</span>/2, about their common out-of-plane [001] crystal axis. (<b>o</b>) In a two-particle system, the particle diameters are Dp, the misorientation angles are angle <span class="html-italic">θ</span>, and the grain boundaries will not form in small misorientation angles (white cell) through rotation and will only form in large misorientation angles (gray cells). Reproduced with permission [<a href="#B87-nanomaterials-11-00241" class="html-bibr">87</a>]. Copyright 2019, Elsevier B.V.</p>
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<p>(<b>a</b>) Scheme of classical and non-classical crystallization. Reproduced with permission [<a href="#B105-nanomaterials-11-00241" class="html-bibr">105</a>]. Copyright 2019, MDPI. (<b>b</b>) Octahedral PbSe nanocrystals grown in the presence of hexadecylamine (HDA) and oleic acid. TEM and HRTEM images of PbSe zigzag nanowires grown in the presence of HDA. Reproduced with permission [<a href="#B58-nanomaterials-11-00241" class="html-bibr">58</a>]. Copyright 2005, American Chemical Society. (<b>c</b>) Scheme of structure and morphology transformation processes for the synthesis of Co<sub>3</sub>O<sub>4</sub> at different temperatures. Reproduced with permission [<a href="#B104-nanomaterials-11-00241" class="html-bibr">104</a>]. Copyright 2013, Elsevier B.V.</p>
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<p>(<b>a</b>) Polarization hysteresis curves of the Na<sub>0.5</sub>K<sub>0.5</sub>NbO<sub>3</sub> ceramic spark plasma sintered at 920 °C for 5 min and then annealed at 900 °C for different times in air: (1) 1 h and (2, 3) 4 h. (<b>b</b>) Microstructure of the Na<sub>0.5</sub>K<sub>0.5</sub>NbO<sub>3</sub> ceramics: (1) Scanning electron microscopy micrograph and (2, 3) transmission electron microscopy micrographs. (<b>c</b>) Density change of the spark plasma sintered sample as a function of spark plasma sintering (SPS) temperature. Reproduced with permission [<a href="#B109-nanomaterials-11-00241" class="html-bibr">109</a>]. Copyright 2005, John Wiley and Sons.</p>
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<p>(<b>a</b>) SEM micrographs illustrating microstructures of (1) pure hydroxyapatite (HAP) and HAP with 2.5wt% of (2) 100% CaO, (3) 55% CaO + 30% P<sub>2</sub>O<sub>5</sub> + 15% Na<sub>2</sub>O, (4) 30% CaO + 30% P<sub>2</sub>O<sub>5</sub> + 40% Na<sub>2</sub>O, and (5) 17.2% CaO + 61.4% P<sub>2</sub>O<sub>5</sub> + 21.4% Na<sub>2</sub>O. (<b>b</b>) Variation in Vickers micro hardness values of sintered compacts of different compositions as a function of their sintered densities. Reproduced with permission [<a href="#B120-nanomaterials-11-00241" class="html-bibr">120</a>]. Copyright 2004, Elsevier. (<b>c</b>–<b>e</b>) 3D models and relative selective laser sintering (SLS) manufactured scaffold for medical application. (<b>f</b>) Micro-computer tomography of human trabecular bone tissue (left) and a mimetic tissue produced by SLS (right). Reproduced with permission [<a href="#B127-nanomaterials-11-00241" class="html-bibr">127</a>]. Copyright 2012, Spring Nature.</p>
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<p>(<b>a</b>) Scheme for the preparation of hydroxyapatite (HA) optical material. (<b>b</b>) HRTEM image of the HA nanorods showing clear crystal lattice (scale bar, 10 nm). The images of mesoporous nanorods (scale bar, 20 nm) and the related selected area electron diffraction. (<b>c</b>) X-ray diffraction (XRD) patterns of the section and surface of HA ceramics prepared at 850 °C, with the increased peak intensity at (002), (004) showing that the grains have a pronounced orientation perpendicular to the pressure direction. Abridged general view (<b>d</b>,<b>e</b>) of the spatial distribution of HA grains c-axis (red arrow lines) in different pressure surfaces, exhibiting a preferable arrangement with their c-axis in the planes overlay perpendicular to the pressure direction; (<b>f</b>) The linear transmittance of HA ceramic with incident light perpendicular to and parallel to pressure directions, respectively. Reproduced with permission [<a href="#B7-nanomaterials-11-00241" class="html-bibr">7</a>]. Copyright 2020, Wiley-VCH.</p>
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16 pages, 6800 KiB  
Article
High Current Field Emission from Large-Area Indium Doped ZnO Nanowire Field Emitter Arrays for Flat-Panel X-ray Source Application
by Yangyang Zhao, Yicong Chen, Guofu Zhang, Runze Zhan, Juncong She, Shaozhi Deng and Jun Chen
Nanomaterials 2021, 11(1), 240; https://doi.org/10.3390/nano11010240 - 18 Jan 2021
Cited by 23 | Viewed by 3286
Abstract
Large-area zinc oxide (ZnO) nanowire arrays have important applications in flat-panel X-ray sources and detectors. Doping is an effective way to enhance the emission current by changing the nanowire conductivity and the lattice structure. In this paper, large-area indium-doped ZnO nanowire arrays were [...] Read more.
Large-area zinc oxide (ZnO) nanowire arrays have important applications in flat-panel X-ray sources and detectors. Doping is an effective way to enhance the emission current by changing the nanowire conductivity and the lattice structure. In this paper, large-area indium-doped ZnO nanowire arrays were prepared on indium-tin-oxide-coated glass substrates by the thermal oxidation method. Doping with indium concentrations up to 1 at% was achieved by directly oxidizing the In-Zn alloy thin film. The growth process was subsequently explained using a self-catalytic vapor-liquid-solid growth mechanism. The field emission measurements show that a high emission current of ~20 mA could be obtained from large-area In-doped sample with a 4.8 × 4.8 cm2 area. This high emission current was attributed to the high crystallinity and conductivity change induced by the indium dopants. Furthermore, the application of these In-doped ZnO nanowire arrays in a flat-panel X-ray source was realized and distinct X-ray imaging was demonstrated. Full article
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<p>Images of ZnO nanowire arrays with indium doping. (<b>a</b>) Photograph consist of glass substrate, indium–tin-oxide (ITO) electrode and the prepared ZnO nanowire field emission arrays (FEAs) with indium doping; (<b>b</b>) top view SEM image of a 4 × 3 In-doped ZnO nanowire pattern array in low magnification; (<b>c<sub>1</sub></b>,<b>c<sub>2</sub></b>) single pattern at different regions in high magnification; and (<b>d</b>) cross-sectional SEM image of a single pattern; (<b>e</b>,<b>f</b>) Statistical results of the length and diameter.</p>
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<p>TEM characterization of a single In-doped ZnO nanowire. (<b>a</b>) Low-resolution TEM image; inset corresponding EDX spectrum. (<b>b</b>) High-resolution TEM image of the sample and selected-area electron diffraction (SAED) pattern (inset). (<b>c<sub>1</sub></b>–<b>c<sub>3</sub></b>) EDX elemental mapping of (<b>c<sub>1</sub></b>) Zn, (<b>c<sub>2</sub></b>) O, and (<b>c<sub>3</sub></b>) In.</p>
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<p>Characterization of ZnO nanowires with indium doping. (<b>a</b>) XRD pattern, (<b>b</b>) XPS spectrum, inset detail of XPS for In 3d enlarged peaks, (<b>c</b>) room-temperature PL spectrum of a single In-doped ZnO nanowire.</p>
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<p>Top-view and cross-sectional SEM images of thin films and nanowires after a growth time of (<b>a</b>,<b>a<sub>1</sub></b>) 0 min (20 °C), (<b>b</b>,<b>b<sub>1</sub></b>) 90 min (250 °C), (<b>c</b>,<b>c<sub>1</sub></b>) 180 min (470 °C), and (<b>d</b>,<b>d<sub>1</sub></b>) 270 min (470 °C); (<b>e</b>) Zn film thickness vs. heated time.</p>
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<p>Schematic diagram of the growth process of In-doped ZnO nanowires. (<b>a</b>) The In-Zn alloy film was deposited on the substrate, (<b>b</b>) indium agglomerates precipitated on the film surface, (<b>c</b>) zinc vaporized from the film, (<b>d</b>) ZnO nanowires grew from the In catalyst, (<b>e</b>) the In-doped ZnO nanowire after growth.</p>
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<p>(<b>a</b>) Field emission curve (J-E) and Fowler-Nordheim (F-N) plot (inset) of ZnO nanowires with indium doping (<b>b</b>,<b>c</b>) Field emission stability of (<b>b</b>) voltage (U) with constant current at 6.5 mA and (<b>c</b>) direct current (I) with constant voltage of 1.02 kV.</p>
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<p>Comparison in the (<b>a</b>) emission current and (<b>b</b>) corresponding current density of nanowires reported in this paper and that reported in the literature (References given with data in square brackets).</p>
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<p>Typical electrical characteristics of an individual In-doped ZnO nanowire, inset is the SEM image during the measurement.</p>
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<p>Characteristics of the flat-panel X-ray source. (<b>a</b>) I–V curve, (Upper Inset) F-N plot, and (Lower Inset) schematic diagram of testing device. (<b>b</b>) Visible light image recorded when the device is operated at a 46 kV anode voltage. (<b>c</b>) Normalized X-ray energy spectra at a 46 kV anode voltage. (<b>d</b>) X-ray dose rate vs. voltage for anode-cathode distance of 20 cm (blue squares) and 25 cm (red circles).</p>
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<p>X-ray images of non-biological and biological samples (<b>a</b>–<b>d</b>). (<b>a</b>) An integrated circuit chip. (<b>b</b>) A calculator, (<b>c</b>) hippocampal specimen and (<b>d</b>) fresh loach. Images of moving metronome needle taken using the X-ray source driven using pulsed high voltage with the pulse width of 100 ms (<b>e</b>) and 10 ms (<b>f</b>).</p>
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12 pages, 3100 KiB  
Article
A TiO2 Coated Carbon Aerogel Derived from Bamboo Pulp Fibers for Enhanced Visible Light Photo-Catalytic Degradation of Methylene Blue
by Jian Zhang, Wei Yuan, Tian Xia, Chenghong Ao, Jiangqi Zhao, Bingxue Huang, Qunhao Wang, Wei Zhang and Canhui Lu
Nanomaterials 2021, 11(1), 239; https://doi.org/10.3390/nano11010239 - 18 Jan 2021
Cited by 27 | Viewed by 3472
Abstract
Carbon aerogels (CA) derived from bamboo cellulose fibers were coupled with TiO2 to form CA/TiO2 hybrids, which exhibited extraordinary performance on the photo-catalytic degradation of methylene blue (MB). The structure and morphology of CA/TiO2 were characterized by field emission scanning [...] Read more.
Carbon aerogels (CA) derived from bamboo cellulose fibers were coupled with TiO2 to form CA/TiO2 hybrids, which exhibited extraordinary performance on the photo-catalytic degradation of methylene blue (MB). The structure and morphology of CA/TiO2 were characterized by field emission scanning electron microscopy, Fourier transform infrared spectroscopy, X-ray photoelectron spectroscopy, X-ray diffraction, and Raman spectrum. The CA displayed a highly porous and interconnected three-dimensional framework structure, while introducing the catalytic active sites of TiO2 onto the aerogel scaffold could remarkably enhance its photo-catalytic activity. The adsorption and photo-catalytic degradation of MB by the CA/TiO2 hybrid were investigated. The maximum adsorption capacity of CA/TiO2 for MB was 18.5 mg/g, which outperformed many similar materials reported in the literature. In addition, compared with other photo-catalysts, the present CA/TiO2 demonstrated superior photo-catalytic performance. Almost 85% of MB in 50 mL solution with a MB concentration of 10 mg/L could be effectively degraded by 15 mg CA/TiO2 in 300 min. Full article
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<p>SEM images of carbon aerogels (CA) (<b>a</b>–<b>c</b>) and CA/TiO<sub>2</sub> (<b>d</b>–<b>f</b>) and energy dispersive X-ray spectroscopy (EDX) results for CA/TiO<sub>2</sub> (<b>g</b>).</p>
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<p>FTIR spectra of CA and CA/TiO<sub>2</sub>.</p>
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<p>Raman spectrum of CA/TiO<sub>2</sub>.</p>
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<p>XRD pattern of CA/TiO<sub>2</sub>.</p>
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<p>XPS spectrum (<b>a</b>) and deconvoluted Ti<sub>2</sub>p spectrum (<b>b</b>) and O1s spectrum (<b>c</b>) of CA/TiO<sub>2</sub>.</p>
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<p>Diffuse reflectance spectrum of CA/TiO<sub>2</sub>.</p>
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<p>Adsorption isotherm of methylene blue (MB).</p>
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<p>Photo-catalytic degradation of MB by CA/TiO<sub>2</sub> and CA. The insert shows the color change of the solution before and after the CA/TiO<sub>2</sub> treatment.</p>
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<p>First-order degradation kinetics plot of MB by CA/TiO<sub>2.</sub></p>
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12 pages, 2162 KiB  
Article
Solvent-Free Mechanochemical Synthesis of ZnO Nanoparticles by High-Energy Ball Milling of ?-Zn(OH)2 Crystals
by Gil Otis, Michal Ejgenberg and Yitzhak Mastai
Nanomaterials 2021, 11(1), 238; https://doi.org/10.3390/nano11010238 - 18 Jan 2021
Cited by 39 | Viewed by 5712
Abstract
A detailed investigation is presented for the solvent-free mechanochemical synthesis of zinc oxide nanoparticles from ε-Zn(OH)2 crystals by high-energy ball milling. Only a few works have ever explored the dry synthetic route from ε-Zn(OH)2 to ZnO. The milling process of ε-Zn(OH) [...] Read more.
A detailed investigation is presented for the solvent-free mechanochemical synthesis of zinc oxide nanoparticles from ε-Zn(OH)2 crystals by high-energy ball milling. Only a few works have ever explored the dry synthetic route from ε-Zn(OH)2 to ZnO. The milling process of ε-Zn(OH)2 was done in ambient conditions with a 1:100 powder/ball mass ratio, and it produced uniform ZnO nanoparticles with sizes of 10–30 nm, based on the milling duration. The process was carefully monitored and the effect of the milling duration on the powder composition, nanoparticle size and strain, optical properties, aggregate size, and material activity was examined using XRD, TEM, DLS, UV-Vis, and FTIR. The mechanism for the transformation of ε-Zn(OH)2 to ZnO was studied by TGA and XPS analysis. The study gave proof for a reaction mechanism starting with a phase transition of crystalline ε-Zn(OH)2 to amorphous Zn(OH)2, followed by decomposition to ZnO and water. To the best of our knowledge, this mechanochemical approach for synthesizing ZnO from ε-Zn(OH)2 is completely novel. ε-Zn(OH)2 crystals are very easy to obtain, and the milling process is done in ambient conditions; therefore, this work provides a simple, cheap, and solvent-free way to produce ZnO nanoparticles in dry conditions. We believe that this study could help to shed some light on the solvent-free transition from ε-Zn(OH)2 to ZnO and that it could offer a new synthetic route for synthesizing ZnO nanoparticles. Full article
(This article belongs to the Section Synthesis, Interfaces and Nanostructures)
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<p>Powder diffraction patterns of zinc oxides: (<b>A</b>) XRD spectra of ε-Zn(OH)<sub>2</sub> (before milling) and milled products with different cycles; (1,0,0), (0,0,2), and (1,0,1) characteristic ZnO peaks are indicated. (<b>B</b>) Peak broadening and shifting of the (1,0,1) characteristic peak of ZnO. (<b>C</b>) Comparison of crystallite size calculated by the Scherrer and Williamson–Hall (WH) methods and lattice strain.</p>
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<p>HRTEM images after 10 cycles indicating ZnO nanoparticle aggregates: (<b>A</b>) Large-scale image showing an aggregate consisting of small ZnO crystallites. (<b>B</b>) Small-scale image of nanocrystallites highlighting a crystallite with d-spacing of 2.81 angstrom fitting the (1,0,0) plane of ZnO (bottom right inset), and a SAED pattern of nanocrystalline aggregates (upper right inset).</p>
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<p>Thermal gravimetric analysis of ZnO milled powders—a detailed analysis of the decomposition steps of samples after 2 (<b>A</b>), 5 (<b>B</b>), 8 (<b>C</b>), and 10 (<b>D</b>) cycles.</p>
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<p>X-ray photoelectron spectroscopy (XPS) analysis of ZnO milled powders—0 1s XPS spectra of ε-Zn(OH)<sub>2</sub> and milled powders examining the oxygen–zinc binding energy.</p>
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<p>Methyl orange (MO) degradation assay. (<b>A</b>) Absorbance spectra of MO before and after exposure to UV radiation for 30 min (purple and yellow lines) and in the presence of powders after 2 (red), 5 (green), 8 (blue), and 10 (orange) cycles. (<b>B</b>) Degradation percentage of MO compared to the dye before UV exposure. Dye concentrations were calculated using the Beer–Lambert law.</p>
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29 pages, 14653 KiB  
Article
Investigations of Shape, Material and Excitation Wavelength Effects on Field Enhancement in SERS Advanced Tips
by Yaakov Mandelbaum, Raz Mottes, Zeev Zalevsky, David Zitoun and Avi Karsenty
Nanomaterials 2021, 11(1), 237; https://doi.org/10.3390/nano11010237 - 18 Jan 2021
Cited by 8 | Viewed by 3418
Abstract
This article, a part of the larger research project of Surface-Enhanced Raman Scattering (SERS), describes an advanced study focusing on the shapes and materials of Tip-Enhanced Raman Scattering (TERS) designated to serve as part of a novel imager device. The initial aim was [...] Read more.
This article, a part of the larger research project of Surface-Enhanced Raman Scattering (SERS), describes an advanced study focusing on the shapes and materials of Tip-Enhanced Raman Scattering (TERS) designated to serve as part of a novel imager device. The initial aim was to define the optimal shape of the “probe”: tip or cavity, round or sharp. The investigations focused on the effect of shape (hemi-sphere, hemispheroid, ellipsoidal cavity, ellipsoidal rod, nano-cone), and the effect of material (Ag, Au, Al) on enhancement, as well as the effect of excitation wavelengths on the electric field. Complementary results were collected: numerical simulations consolidated with analytical models, based on solid assumptions. Preliminary experimental results of fabrication and structural characterization are also presented. Thorough analyses were performed around critical parameters, such as the plasmonic metal—Silver, Aluminium or Gold—using Rakic model, the tip geometry—sphere, spheroid, ellipsoid, nano-cone, nano-shell, rod, cavity—and the geometry of the plasmonic array: cross-talk in multiple nanostructures. These combined outcomes result in an optimized TERS design for a large number of applications. Full article
(This article belongs to the Special Issue Application of SERS for Nanomaterials)
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<p>Refractive index and extinction coefficient of silver (Ag).</p>
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<p>Real and imaginary part of the relative permittivity of silver (Ag).</p>
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<p>Absorption, scattering and extinction cross-section of silver (Ag) spheroid nano-particle.</p>
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<p>Analytical and numerical model comparison for extinction cross-section of silver (Ag) sphere and hemi-sphere.</p>
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<p>Analytical and numerical model comparison for extinction cross-section of silver (Ag) spheroid and hemi-spheroid.</p>
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<p>Illustration example of Comsol simulation of the points (N), (A), and (B). The field enhancement is displayed at the points (N), (A), and (B) and some of their polar pairs of the nano-spheres.</p>
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<p>Tip structure different geometries: (<b>a</b>) hemi-sphere nano-particle; (<b>b</b>) hemi-spheroid nano-particle; (<b>c</b>) cavity; (<b>d</b>) nano-cone; (<b>e</b>) ellipsoidal rod; (<b>f</b>) ellipsoidal cavity; (<b>g</b>) double nano-cone; (<b>h</b>) SERS/TERS square; (<b>i</b>) the physical domain and the port input electric field excitation; (<b>j</b>) the PML domain.</p>
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<p>Tip structure different geometries: (<b>a</b>) hemi-sphere nano-particle; (<b>b</b>) hemi-spheroid nano-particle; (<b>c</b>) cavity; (<b>d</b>) nano-cone; (<b>e</b>) ellipsoidal rod; (<b>f</b>) ellipsoidal cavity; (<b>g</b>) double nano-cone; (<b>h</b>) SERS/TERS square; (<b>i</b>) the physical domain and the port input electric field excitation; (<b>j</b>) the PML domain.</p>
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<p><span class="html-italic">E</span><sup>4</sup> approximation and extinction cross-section for changing polar angle θ in wavelengths range of λ = 250–500 nm. (<b>a</b>) <span class="html-italic">E</span><sup>4</sup> approximation for hemi-sphere; (<b>b</b>) extinction for hemi-sphere; (<b>c</b>) <span class="html-italic">E</span><sup>4</sup> approximation for cavity; (<b>d</b>) extinction for cavity; (<b>e</b>) <span class="html-italic">E</span><sup>4</sup> approximation for hemi-spheroid; (<b>f</b>) extinction for hemi-spheroid; (<b>g</b>) <span class="html-italic">E</span><sup>4</sup> approximation for nano-cone; (<b>h</b>) extinction for nano-cone.</p>
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<p>Ellipsoidal cavity results while changing the polar angle θ in a wavelengths range of λ = 250–500 nm. (<b>a</b>) <span class="html-italic">E</span><sup>4</sup> approximation; (<b>b</b>) extinction cross-section.</p>
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<p>Ellipsoidal rod results while changing the polar angle θ in a wavelengths range of λ = 250–500 nm. (<b>a</b>) <span class="html-italic">E</span><sup>4</sup> approximation; (<b>b</b>) extinction cross-section.</p>
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<p>Double nano-cone results while changing the polar angle θ in a wavelengths range of λ = 250–500 nm. (<b>a</b>) <span class="html-italic">E</span><sup>4</sup> approximation; (<b>b</b>) extinction cross-section.</p>
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<p>Surface-Enhanced Raman Scattering (SERS) EF: comparison between different nano-particle geometries.</p>
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<p>Extinction cross-section: comparison between different nano-particle geometries.</p>
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<p>Field Enhancement vs. wavelength for an incident plane wave on a silver (Ag), gold (Au) and aluminum (Al) 20 nm-radius sphere. The <span class="html-italic">E</span><sup>4</sup> approximation for the electric field enhancement is displayed. Relevant wavelength peaks: silver at λ = 370 nm, gold at λ = 530 nm, aluminum at λ = 175 nm.</p>
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<p>Simulations of silver (<b>a</b>), aluminum (<b>b</b>) and gold (<b>c</b>) nano-particle with the input of electric field in the Y direction and with k vector in the -Z direction.</p>
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<p>Simulations of silver (<b>a</b>), aluminum (<b>b</b>) and gold (<b>c</b>) nano-particle with the input of electric field in the Y direction and with k vector in the -Z direction.</p>
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<p>Simulation of nano-shells with thickness (T) ranging from 1.433 to 8.303 nm. The impinging electric field is polarized in the Y direction as shown by the red arrows and the wave front direction (K vector) is in the -Z direction. Δ = 0.2 (<b>a</b>), Δ = 0.4 (<b>b</b>), Δ = 0.6 (<b>c</b>), and Δ = 0.8 (<b>d</b>), where Δ = 1-(r/R)<sup>3</sup>.</p>
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<p>Simulation of nano-shells with thickness (T) ranging from 1.433 to 8.303 nm. The impinging electric field is polarized in the Y direction as shown by the red arrows and the wave front direction (K vector) is in the -Z direction. Δ = 0.2 (<b>a</b>), Δ = 0.4 (<b>b</b>), Δ = 0.6 (<b>c</b>), and Δ = 0.8 (<b>d</b>), where Δ = 1-(r/R)<sup>3</sup>.</p>
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<p>Enhancement curves for spherical nano-shells with outer radius (R) of 20 nm and inner radius (r) such that the nano-shell thickness is T = R − r. The nano-shells thickness ranges between T(Δ = 0.2) = 1.433 nm and T(Δ = 0.8) = 8.303 nm. The shells are excited by a plane wave. The resonance peak shifts depending on the shell thickness. Moreover, the electric field enhancement gets bigger as the nano-shell thickness decreases.</p>
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<p>Analytical and numerical models for the normalized enhancement factor.</p>
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<p>Simulation configuration of neighboring silver hemi-spheroid.</p>
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<p>Enhancement vs. separation, for four silver hemi-spheroid in a plane wave, polarized orthogonally to axis of separation. Suppression is observed at short distances. At ~110 nm, the radiation field dominates the localized surface plasmon (LSP) (near) field.</p>
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<p>Extinction cross-section vs. separation for four silver spheres in an oscillating electric field in the Y direction.</p>
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<p>The radiation pattern of a dipole oscillator. The field on the axis is parallel to the dipole leading to enhancement.</p>
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<p>Simulation of separated hemi-spheroid nano-particles. (<b>a</b>) Separation of 20 nm; (<b>b</b>) separation of 110 nm. The width of physical geometry W = 250 nm. The electric field polarization is in the Y direction, therefore the localized surface plasmon is excited mostly in that direction. There is less interaction between nano-particles separated in the X direction.</p>
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<p>Simulation of four separated hemi-spheroid particles (separation = 20 nm, 110 nm). The width of physical geometry W = 250 nm. (<b>a</b>) <span class="html-italic">E</span><sup>4</sup> approximation; (<b>b</b>) extinction cross-section.</p>
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<p>SEM pictures of preliminary samples fabricated with FIB technique. (<b>a</b>) Simulation mask of an array of tips before the fabrication of the protrusions; (<b>b</b>) simulation mask of holes array before the fabrication of cavities. (<b>c</b>) Nano-holes square lattice of cavities; (<b>d</b>) nano-holes hexagonal lattice of cavities; (<b>e</b>) nano-protrusions array using FIB; (<b>f</b>) nano-protrusion double-array fabrication using FIB.</p>
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<p>SEM pictures of preliminary samples fabricated with FIB technique. (<b>a</b>) Simulation mask of an array of tips before the fabrication of the protrusions; (<b>b</b>) simulation mask of holes array before the fabrication of cavities. (<b>c</b>) Nano-holes square lattice of cavities; (<b>d</b>) nano-holes hexagonal lattice of cavities; (<b>e</b>) nano-protrusions array using FIB; (<b>f</b>) nano-protrusion double-array fabrication using FIB.</p>
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22 pages, 6456 KiB  
Article
Experimental and Theoretical Studies on Sustainable Synthesis of Gold Sol Displaying Dichroic Effect
by Anshuman Jakhmola, Raffaele Vecchione, Valentina Onesto, Francesco Gentile, Maurizio Celentano and Paolo Antonio Netti
Nanomaterials 2021, 11(1), 236; https://doi.org/10.3390/nano11010236 - 18 Jan 2021
Cited by 19 | Viewed by 4084
Abstract
Gold nanoparticles depending on their shape and mixtures of multiple shapes can exhibit peculiar optical properties, including the dichroic effect typical of the Lycurgus cup, which has puzzled scientists for a long time. Such optical properties have been recently exploited in several fields [...] Read more.
Gold nanoparticles depending on their shape and mixtures of multiple shapes can exhibit peculiar optical properties, including the dichroic effect typical of the Lycurgus cup, which has puzzled scientists for a long time. Such optical properties have been recently exploited in several fields such as paint technology, sensors, dichroic polarizers, display (LCD) devices, laser applications, solar cells and photothermal therapy among others. In this article, we have demonstrated a simple room temperature one-pot synthesis of gold sol displaying a dichroic effect using a slow reduction protocol involving only trisodium citrate as a reducing agent. We found that the dichroic gold sol can be easily formed at room temperature by reducing gold salt by trisodium citrate below a certain critical concentration. The sol displayed an orangish-brown color in scattered/reflected light and violet/blue/indigo/purple/red/pink in transmitted light, depending on the experimental conditions. With minor changes such as the introduction of a third molecule or replacing a small amount of water in the reaction mixture with ethanol, the color of the gold sol under transmitted light changed and a variety of shades of red, pink, cobalt blue, violet, magenta and purple were obtained. The main advantage of the proposed method lies in its simplicity, which involves the identification of the right ratio of the reactants, and simple mixing of reactants at room temperature with no other requirements. TEM micrographs displayed the formation of two main types of particles viz. single crystal gold nanoplates and polycrystalline faceted polyhedron nanoparticles. The mechanism of growth of the nanoplates and faceted polyhedron particles have been described by an enhanced diffusion limited aggregation numerical scheme, where it was assumed that both trisodium citrate and the gold ions in solution undergo a stochastic Brownian motion, and that the evolution of the entire system is regulated by a principle of energy minimization. The predictions of the model matched with the experiments with a good accuracy, indicating that the initial hypothesis is correct. Full article
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<p>Dichroic gold: (<b>a</b>) Dichroic gold synthesized at room temperature by mixing aqueous solution of trisodium citrate and chloroauric acid Au<sup>3+</sup> 500 µL + trisodium citrate 50 µL + water 450 µL. The color of transmitted light is blue while scatter light is golden-brown. (<b>b</b>) Dichromic gold sol prepared by adding a third molecule/solvent in the reaction mixture displaying different shades of golden-brown color in scattered light. Au<sup>3+</sup> 500 µL + trisodium citrate 50 µL in all samples plus (1) water 450 µL + polyvinyl alcohol (PVA) 5 µL, (2) water 450 µL + PVA 20 µL, (3) water 250 µL + EtOH 200 µL + PVA 5 µL, (4) water 250 µL + EtOH 200 µL + PVA 10 µL, (5) water 250µL + EtOH 200 µL + PVA 20 µL, (6) water 450 µL + Dextran 5 µL, (7) water 450 µL + Dextran 20 µL, (8) water 450 µL + polyvinylpyrrolidone (PVP) 5 µL and (9) water 450 µL + PVP 20 µL. (<b>c</b>) Same sol in transmitted light. The colors of transmitted light are (1) pink, (2) red, (3) blue, (4) indigo, (5) violet, (6) magenta, (7) purple, (8) cobalt blue and (9) cobalt blue. (<b>d</b>) Dichoric sol displaying a Tyndall effect when green laser beam was passed through it. (<b>e</b>) UV–Vis kinetics of dichroic sol; inset evolution and growth of plasmon band with respect to time. (<b>f</b>) UV–Vis spectra of different dichroic sols as in (<b>b</b>,<b>c</b>). (<b>g</b>) PVA–dichromic gold composite film on glass surface displaying dichroic effect, the dichroic effect is retained in solid form when dried at 70 °C. C<sub>HAuCl4</sub> = 2.0 mM, C<sub>citrate</sub>= 1.94 mM with molar ratio R = C<sub>citrate</sub>/C<sub>HAuCl4</sub> equal to 0.97 in all samples.</p>
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<p>(<b>a</b>,<b>b</b>) TEM micrographs of dichroic gold at different magnification displaying formation of two different types of nanocrystals, single crystal nanoplates and polycrystalline faceted nanoparticles. (<b>c</b>,<b>d</b>,<b>g</b>) TEM micrographs at different magnification of faceted particles and (<b>f</b>) TEM micrograph of a single hexagonal nanoplate of gold. (<b>e</b>) SAED pattern hexagonal nanoplate displaying single crystal structure. (<b>h</b>) SAED pattern of faceted particle displaying polycrystalline nature and <span class="html-italic">fcc</span> structure.</p>
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<p>(<b>a</b>) SEM images of polyhedral-shaped gold nanoparticles, displaying both nano/micro plates and faceted particles. (<b>b</b>) EDX mapping of same image displaying distribution of gold. (<b>c</b>,<b>d</b>) SEM micrographs of faceted particles at different magnifications. (<b>e</b>) EDX of gold nano/micro plates displaying different elements.</p>
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<p>TEM images of intermediates captured during course of reaction displaying (<b>a</b>–<b>c</b>) aggregates of 10–15 nm gold nanoparticles and (<b>d</b>,<b>e</b>) displaying growth of small 10–15 nm particles probably by atom-by-atom reduction on the surface. Scheme for the formation of gold nano/micro plates and faced polyhedron nanoparticles as seen in TEM images of intermediates is also presented.</p>
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<p>pH variation monitored over time during the dichroic sol synthesis (inset shows the corresponding ln-ln plot).</p>
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<p>The numerical grid where the process of diffusion and aggregation is simulated. In the grid, the movement of a particle is discretized in finite steps. The aggregate is given by the accumulation of smaller elements on a seed. The probability of adhesion is proportional to the number of broken bonds of each element of the aggregate (<b>a</b>). The trajectory of individual particles in the domain is a random walk (<b>b</b>).</p>
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<p>The initial seeds around which the numerical aggregates were formed and coordination number associated with those seeds (<b>a</b>). Time evolution of the aggregate for different initial seeds enforcing the energy minimization condition in the diffusion limited aggregation algorithm (<b>b</b>). Time evolution of the aggregate for different initial seeds without the energy minimization condition in the diffusion limited aggregation algorithm (<b>c</b>).</p>
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<p>Growth dynamics of a numerical aggregate: for this configuration, the initial seed is a point (<b>a</b>). Growth dynamics of the real physical prototype determined as the variation over time of the absorbance peak measured through UV spectroscopy (<b>b</b>). Curves of growth of the numerical aggregates for different types of the initial seed and sticking probability <span class="html-italic">sp</span> = 1 (<b>c</b>). Curves of growth of the numerical aggregates for different types of the initial seed and sticking probability <span class="html-italic">sp</span> = 0.1 (<b>d</b>). Steady state value of the aggregate mass (<b>e</b>) and time to the steady state (<b>f</b>) as a function of the sticking probability.</p>
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<p>Shape of the initial seeds (<b>a</b>) and the numerical aggregates obtained with (<b>b</b>) and without (<b>c</b>), the energy optimization condition. Density–density correlation function derived for the numerical aggregates (<b>d</b>).</p>
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<p>Distance among different numerical aggregates determined canonical warping distance metrics.</p>
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<p>SEM and TEM images of multifaceted gold nanoparticles at different times from the inception of synthesis (<b>a</b>). Corresponding numerical aggregates generated by the energy minimization diffusion-limited aggregation (EM DLA) algorithm (<b>b</b>). Normalized curves of growth of a numerical aggregate starting from a hexagon as a seed, for different values of the sticking probability, compared to the nondimensional growth profile of real gold nanoparticles (<b>c</b>). Rate of growth determined at the early stage of the process for the numerical aggregates at different values of sticking probability: the rate of growth of real nanoparticles is used in the diagram to retrieve the value of sticking probability that leads to the best matching between the predictions of the model template and experimental data (<b>d</b>). Particle size distribution determined for the real gold multifaceted nanoparticles (<b>e</b>) and the numerical aggregates (<b>f</b>); both distributions are skewed to the right.</p>
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17 pages, 8854 KiB  
Article
Stabilization of Calcium Oxalate Precursors during the Pre- and Post-Nucleation Stages with Poly(acrylic acid)
by Felipe Díaz-Soler, Carlos Rodriguez-Navarro, Encarnación Ruiz-Agudo and Andrónico Neira-Carrillo
Nanomaterials 2021, 11(1), 235; https://doi.org/10.3390/nano11010235 - 18 Jan 2021
Cited by 8 | Viewed by 2698
Abstract
In this work, calcium oxalate (CaOx) precursors were stabilized by poly(acrylic acid) (PAA) as an additive under in vitro crystallization assays involving the formation of pre-nucleation clusters of CaOx via a non-classical crystallization (NCC) pathway. The in vitro crystallization of CaOx was carried [...] Read more.
In this work, calcium oxalate (CaOx) precursors were stabilized by poly(acrylic acid) (PAA) as an additive under in vitro crystallization assays involving the formation of pre-nucleation clusters of CaOx via a non-classical crystallization (NCC) pathway. The in vitro crystallization of CaOx was carried out in the presence of 10, 50 and 100 mg/L PAA by using automatic calcium potentiometric titration experiments at a constant pH of 6.7 at 20 °C. The results confirmed the successful stabilization of amorphous calcium oxalate II and III (ACOII and ACO III) nanoparticles formed after PNC in the presence of PAA and suggest the participation and stabilization of polymer-induced liquid-precursor (PILP) in the presence of PAA. We demonstrated that PAA stabilizes CaOx precursors with size in the range of 20–400 nm. PAA additive plays a key role in the in vitro crystallization of CaOx stabilizing multi-ion complexes in the pre-nucleation stage, thereby delaying the nucleation of ACO nanoparticles. Indeed, PAA additive favors the formation of more hydrated and soluble phase of ACO nanoparticles that are bound by electrostatic interactions to carboxylic acid groups of PAA during the post-nucleation stage. These findings may help to a better understanding of the pathological mineralization resulting in urolithiasis in mammals. Full article
(This article belongs to the Section Synthesis, Interfaces and Nanostructures)
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<p>Time development of free Ca<sup>2+</sup> ion concentration in titration experiments of CaOx (solid line) and pure water (dashed line) in the absence and presence of three concentrations of PAA as additive. (<b>a</b>) Titration experiments of CaOx. (<b>b</b>) Titration experiments of CaOx and pure water. Each vertical arrow indicates the corresponding sample collection time for TEM analysis.</p>
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<p>Time development of the ion activity product in titration experiments of CaOx in the absence and presence of three concentrations of PAA as an additive at pH 6.7.</p>
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<p>ACO particles obtained during the early stages of nucleation in the absence of PAA. (<b>a</b>) TEM images of ACO particles, (<b>b</b>) TEM images and SAED pattern of ACO nanoparticles. And in presence of PAA with (<b>c</b>) 10 mg/L PAA, (<b>d</b>) 50 mg/L, (<b>e</b>) 100 mg/L PAA, (<b>f</b>) ACO nanoparticle showing different electron-densities.</p>
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<p>In situ DLS analysis of particle size distribution (PSD) of particles formed during the titration experiments in the absence and in the presence of three concentrations of PAA.</p>
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<p>XRD patterns of CaOx particles obtained via titration experiments in the absence (control) and in the presence of PAA in the post-nucleation stage at 500, 1200 and 6000 s. (<b>a</b>) control, (<b>b</b>) with 10 mg/L PAA, (<b>c</b>) with 50 mg/L PAA, (<b>d</b>) with 100 mg/L PAA. The symbols of •, □ and <span style="color:red">♦</span> indicate COM, COD and COT, respectively.</p>
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<p>FTIR spectra of CaOx particles obtained in post-nucleation stage at 500, 1200 and 6000 s. (<b>a</b>) without PAA, (<b>b</b>) with 10 mg/L PAA, (<b>c</b>) with 50 mg/L PAA, (<b>d</b>) with 100 mg/L PAA. Light blue and orange shaded bars indicate the characteristic absorption bands of COM and the absorption bands of coordinated water molecules in the COD and COT hydrates, respectively.</p>
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<p>CaOx precipitates obtained during the post-nucleation stage in the absence of PAA. (<b>a</b>,<b>b</b>) TEM image and SAED pattern of hexagonal ACO nanoparticles, (<b>c</b>,<b>d</b>) FESEM images of different nanoparticles composed of platy euhedral nanoparticles.</p>
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<p>CaOx precipitates obtained during the post-nucleation stage in the presence of PAA. (<b>a</b>,<b>b</b>) TEM image and SAED study of ACO nanoparticles, (<b>c</b>–<b>f</b>) FESEM images of different nanoparticles and crystals. Red arrows indicate interactions between rhomboid crystal, droplets and filaments in (<b>b</b>).</p>
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<p>Illustration of the in vitro crystallization of CaOx showing the resultant nano/micro particles during pre-and post-nucleation stages of CaOx and tentative molecular mechanism for the stabilization of amorphous ACO nanoparticles.</p>
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18 pages, 6779 KiB  
Article
Synthesis of Nanoparticles by Spark Discharge as a Facile and Versatile Technique of Preparing Highly Conductive Pt Nano-Ink for Printed Electronics
by Alexey A. Efimov, Pavel V. Arsenov, Vladislav I. Borisov, Arseny I. Buchnev, Anna A. Lizunova, Denis V. Kornyushin, Sergey S. Tikhonov, Andrey G. Musaev, Maxim N. Urazov, Mikhail I. Shcherbakov, Denis V. Spirin and Victor V. Ivanov
Nanomaterials 2021, 11(1), 234; https://doi.org/10.3390/nano11010234 - 18 Jan 2021
Cited by 29 | Viewed by 5660
Abstract
A cost-effective, scalable and versatile method of preparing nano-ink without hazardous chemical precursors is a prerequisite for widespread adoption of printed electronics. Precursor-free synthesis by spark discharge is promising for this purpose. The synthesis of platinum nanoparticles (PtNPs) using a spark discharge under [...] Read more.
A cost-effective, scalable and versatile method of preparing nano-ink without hazardous chemical precursors is a prerequisite for widespread adoption of printed electronics. Precursor-free synthesis by spark discharge is promising for this purpose. The synthesis of platinum nanoparticles (PtNPs) using a spark discharge under Ar, N2, and air has been investigated to prepare highly conductive nano-ink. The size, chemical composition, and mass production rate of PtNPs significantly depended on the carrier gas. Pure metallic PtNPs with sizes of 5.5 ± 1.8 and 7.1 ± 2.4 nm were formed under Ar and N2, respectively. PtNPs with sizes of 18.2 ± 9.0 nm produced using air consisted of amorphous oxide PtO and metallic Pt. The mass production rates of PtNPs were 53 ± 6, 366 ± 59, and 490 ± 36 mg/h using a spark discharge under Ar, N2, and air, respectively. It was found that the energy dissipated in the spark gap is not a significant parameter that determines the mass production rate. Stable Pt nano-ink (25 wt.%) was prepared only on the basis of PtNPs synthesized under air. Narrow (about 30 ?m) and conductive Pt lines were formed by the aerosol jet printing with prepared nano-ink. The resistivity of the Pt lines sintered at 750 °C was (1.2 ± 0.1)·10?7 ?·m, which is about 1.1 times higher than that of bulk Pt. Full article
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<p>(<b>a</b>) Scheme of gas-phase synthesis of nanoparticles for the preparation of platinum nano-ink, (<b>b</b>) photograph and (<b>c</b>) equivalent electrical circuit of the spark discharge generator (SDG).</p>
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<p>TEM images of aggregates, primary and individual spherical platinum nanoparticles (PtNPs) synthesized by SDG in various gases: (<b>a</b>,<b>b</b>) Ar, (<b>c</b>,<b>d</b>) N<sub>2</sub>, and (<b>e</b>,<b>f</b>) air. The insets show the corresponding electron diffraction patterns.</p>
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<p>SEM images and EDX spectra of PtNPs synthesized by spark discharge under (<b>a</b>) Ar, (<b>b</b>) N<sub>2</sub> and (<b>c</b>) air.</p>
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<p>Histograms of the particle size distribution of primary Pt nanoparticles synthesized by spark discharge under Ar, N<sub>2</sub>, and air. Histograms are determined from TEM images and approximated by a lognormal function.</p>
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<p>Particle size distributions of Pt aggregates synthesized by spark discharge under Ar, N<sub>2</sub> and air. The measurements were performed using an aerosol spectrometer.</p>
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<p>X-ray photoelectron spectra of PtNPs synthesized by spark discharge under Ar, N<sub>2</sub> and air.</p>
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<p>EDX profile of Pt nanoparticle synthesized by spark discharge under air. The inset shows the TEM image of the measured platinum nanoparticle and the corresponding scan line.</p>
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<p>Oscillograms of voltages <span class="html-italic">U</span> (<span class="html-italic">t</span>) measured between platinum electrodes during a spark discharge under Ar, N<sub>2</sub> and air.</p>
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<p>Photo of the prepared suspensions (nano-inks) with Pt nanoparticles (25 wt.%) dispersed in ethylene glycol (EG) with polyvinylpyrrolidone (PVP).</p>
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<p>Profiles and corresponding optical images (on inserts) of platinum lines formed by AJP at various values of <span class="html-italic">T</span><sub>s</sub> equal to (<b>a</b>) 25 °C, (<b>b</b>) 50 °C, (<b>c</b>) 100 °C, and (<b>d</b>) 150 °C.</p>
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<p>Dependence of the resistivity of platinum lines on <span class="html-italic">T</span><sub>sint</sub> and the corresponding SEM images of the surface of the sintered lines (inset).</p>
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<p>(<b>a</b>) Photo and (<b>b</b>) thermogram of curved Pt-microheater printed on a 20 μm thick low-temperature co-fired ceramic (LTCC) membrane.</p>
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13 pages, 2851 KiB  
Article
Au/CdS Core-Shell Sensitized Actinomorphic Flower-Like ZnO Nanorods for Enhanced Photocatalytic Water Splitting Performance
by Ying Li, Tie Liu, Shuang Feng, Wenshu Yang, Ying Zhu, Yingying Zhao, Zhiyan Liu, Haibin Yang and Wuyou Fu
Nanomaterials 2021, 11(1), 233; https://doi.org/10.3390/nano11010233 - 17 Jan 2021
Cited by 11 | Viewed by 3061
Abstract
Herein, a novel actinomorphic flower-like ZnO/Au/CdS nanorods ternary composite photocatalyst is prepared to extend the light-responsive range, reduce the photogenerated charge carriers recombination, and ultimately improve the water splitting performance. Flower-like ZnO nanorods are synthesized by a chemical bath method and the CdS [...] Read more.
Herein, a novel actinomorphic flower-like ZnO/Au/CdS nanorods ternary composite photocatalyst is prepared to extend the light-responsive range, reduce the photogenerated charge carriers recombination, and ultimately improve the water splitting performance. Flower-like ZnO nanorods are synthesized by a chemical bath method and the CdS nanoparticles are sensitized by successive ionic layer adsorption and reaction method. Then the Au nanoparticles as co-catalysts are introduced by the photodeposition method to modify the interface of ZnO/CdS for reducing the photogenerated electron recombination rate and further improving the performance of water splitting. Detailed characterizations and measurements are employed to analyse the crystallinity, morphology, composition, and optical properties of the flower-like ZnO/Au/CdS nanorods samples. As a result, the flower-like ZnO/Au/CdS nanorod samples present significantly enhanced water splitting performance with a high gas evolution rate of 502.2 μmol/g/h, which is about 22.5 and 1.5 times higher than that of the pure ZnO sample and ZnO/CdS sample. The results demonstrate that the flower-like ZnO/Au/CdS nanorods ternary composite materials have great application potential in photocatalytic water splitting for the hydrogen evolution field. Full article
(This article belongs to the Section Energy and Catalysis)
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<p>XRD patterns of (<b>a</b>) ZnO; (<b>b</b>) ZnO/Au; (<b>c</b>) ZnO/CdS; and (<b>d</b>) ZnO/Au/CdS samples. Inset: magnification images of a portion of the XRD pattern.</p>
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<p>FESEM images of (<b>a</b>) ZnO sample and (<b>b</b>) ZnO/Au/CdS sample; TEM images of (<b>c</b>) ZnO sample and (<b>d</b>,<b>e</b>) ZnO/Au/CdS sample; (<b>f</b>) HRTEM image of ZnO/Au/CdS sample.</p>
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<p>(<b>a</b>–<b>f</b>) EDS mapping images of the ZnO/Au/CdS sample; and (<b>g</b>) EDS image of the ZnO/Au/CdS sample.</p>
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<p>(<b>a</b>) Zn 2p, (<b>b</b>) Au 4f-Zn 3p, (<b>c</b>) Cd 3d, and (<b>d</b>) S 2p peaks in XPS spectra of ZnO, ZnO/Au and ZnO/Au/CdS samples, respectively; (<b>e</b>) Au 4f-Zn 3p peaks of ZnO/Au sample and (<b>f</b>) S 2p peaks of ZnO/Au/CdS sample.</p>
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<p>(<b>a</b>) UV-vis absorption spectra and (<b>b</b>) (<span class="html-italic">ahv</span>)<sup>2</sup>-photon energy curves of the ZnO, ZnO/Au, ZnO/CdS, and ZnO/Au/CdS samples.</p>
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<p>Transient photocurrent response of ZnO, ZnO/Au, ZnO/CdS and ZnO/Au/CdS sample.</p>
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<p>Photoluminescence (PL) spectra of ZnO, ZnO/Au, ZnO/CdS and ZnO/Au/CdS samples.</p>
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<p>(<b>a</b>) The amounts of gas evolution of the ZnO, ZnO/Au, ZnO/CdS and ZnO/Au/CdS samples (100 mg of catalyst for 4 h); (<b>b</b>) the cycling stability of the ZnO/Au/CdS photocatalyst (4 h as a cycle).</p>
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<p>Schematic illustration of charge transfer process and gas evolution mechanism of ZnO/Au/CdS sample.</p>
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16 pages, 3639 KiB  
Review
Carbon Dots-Based Logic Gates
by Shweta Pawar, Hamootal Duadi, Yafit Fleger and Dror Fixler
Nanomaterials 2021, 11(1), 232; https://doi.org/10.3390/nano11010232 - 17 Jan 2021
Cited by 27 | Viewed by 4535
Abstract
Carbon dots (CDs)-based logic gates are smart nanoprobes that can respond to various analytes such as metal cations, anions, amino acids, pesticides, antioxidants, etc. Most of these logic gates are based on fluorescence techniques because they are inexpensive, give an instant response, and [...] Read more.
Carbon dots (CDs)-based logic gates are smart nanoprobes that can respond to various analytes such as metal cations, anions, amino acids, pesticides, antioxidants, etc. Most of these logic gates are based on fluorescence techniques because they are inexpensive, give an instant response, and highly sensitive. Computations based on molecular logic can lead to advancement in modern science. This review focuses on different logic functions based on the sensing abilities of CDs and their synthesis. We also discuss the sensing mechanism of these logic gates and bring different types of possible logic operations. This review envisions that CDs-based logic gates have a promising future in computing nanodevices. In addition, we cover the advancement in CDs-based logic gates with the focus of understanding the fundamentals of how CDs have the potential for performing various logic functions depending upon their different categories. Full article
(This article belongs to the Special Issue Carbon-Based Nanocomposites for Biosensing Approaches)
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<p>Carbon dots and their application in logic function based on their sensing ability.</p>
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<p>Different categories of carbon dots (CDs)-based logic gates according to their output. I. Single output, where only one output is generated. II. Combinational outputs are the integration of simple logic operations to obtain the complex combinational output. III. Sequential output, which responds to multiple inputs but with different stages of activation that should happen in a predestined order. IV. Reversible systems can switch between ON and OFF states depending upon the input added to the system.</p>
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<p>Mechanism of sensing CDs based logic systems with photoinduced electron transfer (PET), fluorescence resonance energy transfer (FRET), and inner filter effect (IFE) process for quenching and recovery by interactions with recovery agents.</p>
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<p>Five different categories of CDs design for logic function.</p>
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<p>Schematic diagram of D-Penicillamine (D-PA) detection by pristine CDs and its AND logic gate function. Reproduced from ref [<a href="#B65-nanomaterials-11-00232" class="html-bibr">65</a>] with permission of Sensors and Actuators, B: Chemical copyright 2016.</p>
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<p>Functionalized CDs (COOH and amine functionalization) used for the detection of Fe<sup>3+</sup>, Zn<sup>2+</sup> cations, and S<sub>2</sub>O<sub>3</sub><sup>2-</sup>, PO<sub>4</sub><sup>3-</sup> anions with its multiple logic operations. Reproduced from ref [<a href="#B35-nanomaterials-11-00232" class="html-bibr">35</a>] with permission of Scientific Reports copyright 2015.</p>
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<p>Schematic diagram of the formation process of N-CDs and detection for chlorpromazine hydrochloride (CPH). Reproduced from ref [<a href="#B70-nanomaterials-11-00232" class="html-bibr">70</a>] with permission of the Journal of Photochemistry and Photobiology A: Chemistry copyright 2019.</p>
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<p>(<b>i</b>) Schematic illustration of multifunctional N-S@RCD. (<b>ii</b>) “INHIBIT” logic function using N-S@RCD. (<b>a</b>) Truth table, (<b>b</b>) fluorescence response of N-S@RCD under different inputs, and (<b>c</b>) Symbol of INHIBIT logic. Reproduced from ref [<a href="#B73-nanomaterials-11-00232" class="html-bibr">73</a>] with permission of the Carbon copyright 2018.</p>
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13 pages, 6160 KiB  
Article
The Adsorption of H2 and C2H2 on Ge-Doped and Cr-Doped Graphene Structures: A DFT Study
by Yiming Liao, Ruochen Peng, Shudi Peng, Wen Zeng and Qu Zhou
Nanomaterials 2021, 11(1), 231; https://doi.org/10.3390/nano11010231 - 16 Jan 2021
Cited by 31 | Viewed by 3443
Abstract
In order to find an excellent sensing material for dissolved gases in transformer oil, the adsorption structures of intrinsic graphene (IG), Ge-doped graphene (GeG), and Cr-doped graphene (CrG) to H2 and C2H2 gas molecules were built. It was found [...] Read more.
In order to find an excellent sensing material for dissolved gases in transformer oil, the adsorption structures of intrinsic graphene (IG), Ge-doped graphene (GeG), and Cr-doped graphene (CrG) to H2 and C2H2 gas molecules were built. It was found that the doping site right above C atom (T) was the most stable structure by studying three potential doping positions of the Ge and Cr atom on the graphene surface. Then, the structural parameters, density of states, and difference state density of these adsorption systems were calculated and analyzed based on the density functional calculations. The results show that the adsorption properties of GeG and CrG systems for H2 and C2H2 are obviously better than the IG system. Furthermore, by comparing the two doping systems, CrG system exhibits more outstanding adsorption performances to H2 and C2H2, especially for C2H2 gas. Finally, the highest adsorption energy (−1.436 eV) and the shortest adsorption distance (1.981 Å) indicate that Cr-doped graphene is promising in the field of C2H2 gas-sensing detection. Full article
(This article belongs to the Special Issue State-of-the-Art Nanomaterials and Nanotechnology in China)
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<p>The structures of H<sub>2</sub> (<b>a</b>) and C<sub>2</sub>H<sub>2</sub> (<b>b</b>).</p>
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<p>Three potential doping sites of graphene.</p>
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<p>The optimized structure of Ge-doped graphene (GeG) at T doping site (<b>a</b>) top view (<b>b</b>) side view.</p>
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<p>The total density of state (TDOS) (<b>a</b>) and partial density of state (PDOS) (<b>b</b>) of GeG system at T doping site.</p>
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<p>The optimized structure of Cr-doped graphene (CrG) at T doping site (<b>a</b>) top view (<b>b</b>) side view.</p>
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<p>The TDOS (<b>a</b>) and PDOS (<b>b</b>) of CrG system at T doping site. The “+” for alpha-spin, “−” for beta-spin in the TDOS plot.</p>
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<p>The optimal structures of H<sub>2</sub> adsorbed on IG (<b>a</b>,<b>d</b>), GeG (<b>b</b>,<b>e</b>), and CrG (<b>c</b>,<b>f</b>) systems.</p>
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<p>The TDOS and PDOS of H<sub>2</sub> adsorbed on IG (<b>a</b>,<b>b</b>), GeG (<b>c</b>,<b>d</b>), and CrG (<b>e</b>,<b>f</b>).</p>
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<p>The charge density difference of CrG system.</p>
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<p>The optimized structures of C<sub>2</sub>H<sub>2</sub> adsorbed on IG (<b>a</b>,<b>d</b>), GeG (<b>b</b>,<b>e</b>), and CrG (<b>c</b>,<b>f</b>) systems.</p>
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<p>The TDOS and PDOS of C<sub>2</sub>H<sub>2</sub> adsorbed on IG (<b>a</b>,<b>b</b>), GeG (<b>c</b>,<b>d</b>) and CrG (<b>e</b>,<b>f</b>).</p>
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<p>The TDOS and PDOS of C<sub>2</sub>H<sub>2</sub> adsorbed on IG (<b>a</b>,<b>b</b>), GeG (<b>c</b>,<b>d</b>) and CrG (<b>e</b>,<b>f</b>).</p>
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<p>The charge density difference of the C<sub>2</sub>H<sub>2</sub> molecule on GeG (<b>a</b>) and CrG (<b>b</b>) systems.</p>
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21 pages, 4709 KiB  
Article
Colloidally Stable P(DMA-AGME)-Ale-Coated Gd(Tb)F3:Tb3+(Gd3+),Yb3+,Nd3+ Nanoparticles as a Multimodal Contrast Agent for Down- and Upconversion Luminescence, Magnetic Resonance Imaging, and Computed Tomography
by Oleksandr Shapoval, Viktoriia Oleksa, Miroslav Šlouf, Volodymyr Lobaz, Olga Trhlíková, Marcela Filipová, Olga Janoušková, Hana Engstová, Jan Pankrác, Adam Modrý, Vít Herynek, Petr Ježek, Luděk Šefc and Daniel Horák
Nanomaterials 2021, 11(1), 230; https://doi.org/10.3390/nano11010230 - 16 Jan 2021
Cited by 14 | Viewed by 4014
Abstract
Multimodal imaging, integrating several modalities including down- and up-conversion luminescence, T1- and T2(T2*)-weighted MRI, and CT contrasting in one system, is very promising for improved diagnosis of severe medical disorders. To reach the goal, it is [...] Read more.
Multimodal imaging, integrating several modalities including down- and up-conversion luminescence, T1- and T2(T2*)-weighted MRI, and CT contrasting in one system, is very promising for improved diagnosis of severe medical disorders. To reach the goal, it is necessary to develop suitable nanoparticles that are highly colloidally stable in biologically relevant media. Here, hydrophilic poly(N,N-dimethylacrylamide-N-acryloylglycine methyl ester)-alendronate-[P(DMA-AGME)-Ale]-coated Gd(Tb)F3:Tb3+(Gd3+),Yb3+,Nd3+ nanoparticles were synthesized by a coprecipitation method in ethylene glycol (EG) followed by coating with the polymer. The particles were tho-roughly characterized by a dynamic light scattering (DLS), transmission electron microscopy (TEM), Fourier-transform infrared spectroscopy (FTIR), thermogravimetric analysis (TGA), X-ray energy dispersive spectroscopy (EDAX), selected area electron diffraction (SAED), elemental ana-lysis and fluorescence spectroscopy. Aqueous particle dispersions exhibited excellent colloidal stability in water and physiological buffers. In vitro toxicity assessments suggested no or only mild toxicity of the surface-engineered Gd(Tb)F3:Tb3+(Gd3+),Yb3+,Nd3+ particles in a wide range of concentrations. Internalization of the particles by several types of cells, including HeLa, HF, HepG2, and INS, was confirmed by a down- and up-conversion confocal microscopy. Newly developed particles thus proved to be an efficient contrast agent for fluorescence imaging, T1- and T2(T2*)-weighted magnetic resonance imaging (MRI), and computed tomography (CT). Full article
(This article belongs to the Special Issue Nanomaterials for Contrast Agent and Biomedical Imaging)
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<p>Chemical structure of alendronate-modified poly(<span class="html-italic">N</span>,<span class="html-italic">N</span>-dimethylacrylamide-<span class="html-italic">co-N</span>-acryloylglycine methyl ester).</p>
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<p>Dependence of hydrodynamic diameter <span class="html-italic">D</span><sub>h</sub> of P(DMA-AGME)-Ale-coated GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> (red) and TbF<sub>3</sub>:Gd<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> nanoparticles (black) in (<b>a</b>) water and (<b>b</b>) PBS and NaAc buffers. The particles were prepared at reaction temperature 75 °C.</p>
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<p>Dependence of (<b>a</b>,<b>c</b>) hydrodynamic diameter <span class="html-italic">D</span><sub>h</sub> and (<b>b</b>,<b>d</b>) ζ-potential of GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles on (<b>a</b>,<b>b</b>) pH and (<b>c</b>,<b>d</b>) NaCl concentration.</p>
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<p>Characterization of P(DMA-AGME)-Ale-coated (<b>a</b>–<b>c</b>) GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> and (<b>d</b>–<b>f</b>) TbF<sub>3</sub>:Gd<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> nanoparticles. (<b>a</b>,<b>d</b>) TEM micrographs of the nanoparticles with insets showing their diffraction patterns, (<b>b</b>,<b>e</b>) TEM/EDX spectra, and (<b>c</b>,<b>f</b>) comparison of experimental selected electron diffraction patterns (TEM/SAED) with calculated powder X-ray diffraction patterns (PXRD) of orthorhombic GdF<sub>3</sub> and TbF<sub>3</sub> structures; the <span class="html-italic">hk</span>0 diffractions, which were stronger in TEM/SAED than in PXRD due to preferred orientation of nanocrystals, are marked with bold font.</p>
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<p>(<b>a</b>) DC and (<b>b</b>) UC photoluminescence emission spectra of P(DMA-AGME)-Ale-coated GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> (red) and TbF<sub>3</sub>:Gd<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup> nanoparticles (black) excited at (<b>a</b>) 272 nm (for GdF<sub>3</sub>:Tb<sup>3+</sup>) or 350 nm (for TbF<sub>3</sub>:Gd<sup>3+</sup>) and (<b>b</b>) 980 nm; particle concentration 1 mg/mL and power density of up-conversion luminescence 5 W/cm<sup>2</sup>.</p>
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<p>Intracellular uptake of (<b>a</b>–<b>f</b>) TbF<sub>3</sub>:Gd<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale and (<b>g</b>–<b>l</b>) GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles by (<b>d</b>–<b>f</b>,<b>j</b>–<b>l</b>) Hela and (<b>a</b>–<b>c</b>,<b>g</b>–<b>i</b>) HF cells. (<b>a</b>,<b>d</b>,<b>g</b>,<b>j</b>) CellMask™ deep red-stained cell membranes were visualized in red channel and (<b>b</b>,<b>e</b>,<b>h</b>,<b>k</b>) nanoparticles were visualized in blue channel. (<b>c</b>,<b>f</b>,<b>i</b>,<b>l</b>) Both channels were merged.</p>
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<p>(<b>a</b>–<b>f</b>) Confocal micrographs of distribution of GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles in HepG2 cells at 808 nm excitation with a laser power of 30–50 mW. (<b>d</b>–<b>f</b>) Detailed micrographs of (<b>a</b>–<b>c</b>). (<b>a</b>,<b>d</b>) CellMask™ deep red-stained cell membrane, (<b>b</b>,<b>e</b>) nanoparticles (green), and (<b>c</b>,<b>f</b>) overlay of (<b>a</b>,<b>b</b>) and (<b>d</b>,<b>e</b>), respectively.</p>
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<p>(<b>a</b>) <span class="html-italic">T</span><sub>1</sub>- and (<b>b</b>) <span class="html-italic">T</span><sub>2</sub>*-weighted MR images of the mouse before retroorbital administration of TbF<sub>3</sub>:Gd<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles and in several time intervals after the administration. (<b>a</b>) The signal in the liver on the <span class="html-italic">T</span><sub>1</sub>-weighted image moderately increased shortly after the administration due to a weak <span class="html-italic">T</span><sub>1</sub> effect, while (<b>b</b>) the signal on the <span class="html-italic">T</span><sub>2</sub>*-weighted MR image of the liver and spleen substantially decreased due to nanoparticle accumulation in the organs. The nanoparticles were slowly excreted from the liver after one day of post-administration; however, signal hypointensity was noticeable even one week after the administration.</p>
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<p>(<b>a</b>) <span class="html-italic">T</span><sub>1</sub>-weighted and (<b>b</b>) <span class="html-italic">T</span><sub>2</sub>*-weighted MR images of the mouse before retroorbital admi-nistration of GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles and in several time intervals after the administration. (<b>a</b>) The signal in the liver on the <span class="html-italic">T</span><sub>1</sub>-weighted image substantially increased shortly after the administration due to a strong <span class="html-italic">T</span><sub>1</sub> effect, while (<b>b</b>) the signal on the <span class="html-italic">T</span><sub>2</sub>*-weighted MR image in the liver and spleen decreased due to nanoparticle accumulation in the organs. Slow excretion of the nanoparticles from the liver was observed after one day post-admi-nistration.</p>
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<p>Coronal CT images of the mouse (<b>a</b>,<b>c</b>) before and (<b>b</b>,<b>d</b>) after administration of GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale nanoparticles; (<b>c</b>,<b>d</b>) enlarged CT view of the abdomen.</p>
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<p>In vivo fluorescence imaging of the mouse after retroorbital administration of GdF<sub>3</sub>:Tb<sup>3+</sup>,Yb<sup>3+</sup>,Nd<sup>3+</sup>@P(DMA-AGME)-Ale-Cy7 nanoparticles.</p>
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14 pages, 1719 KiB  
Article
Single and Repeated Applications of Cerium Oxide Nanoparticles Differently Affect the Growth and Biomass Accumulation of Silene flos-cuculi L. (Caryophyllaceae)
by Daniel Lizzi, Alessandro Mattiello, Barbara Piani, Emanuele Gava, Guido Fellet and Luca Marchiol
Nanomaterials 2021, 11(1), 229; https://doi.org/10.3390/nano11010229 - 16 Jan 2021
Cited by 7 | Viewed by 2396
Abstract
Cerium oxide nanoparticles (nCeO2) have a wide variety of applications in industry. Models demonstrated that nCeO2 can reach environmental compartments. Studies regarding the relationships between plants and nCeO2 considered only crop species, whereas a relevant [...] Read more.
Cerium oxide nanoparticles (nCeO2) have a wide variety of applications in industry. Models demonstrated that nCeO2 can reach environmental compartments. Studies regarding the relationships between plants and nCeO2 considered only crop species, whereas a relevant knowledge gap exists regarding wild plant species. Specimens of Silene flos-cuculi (Caryophyllaceae) were grown in greenhouse conditions in a substrate amended with a single dose (D1) and two and three doses (D2 and D3) of 20 mg kg−1 and 200 mg kg−1nCeO2 suspensions, respectively. sp-ICP-MS and ICP-MS data demonstrated that nCeO2 was taken up by plant roots and translocated towards aerial plant fractions. Biometric variables showed that plants responded negatively to the treatments with a shortage in biomass of roots and stems. Although not at relevant concentrations, Ce was accumulated mainly in roots and plant leaves. Full article
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<p>(<b>A</b>) Experimental setup showing the combination of treatments: control, single-, double-, and triple-dosed plants (Ctrl, D1, D2, and D3, respectively); (<b>B</b>) <span class="html-italic">S. flos-cuculi</span> plants at 40 DSE.</p>
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<p>(<b>A</b>) Particle size distribution obtained by dynamic light scattering (DLS). (<b>B</b>) Transmission electron microscopy (TEM) image of <span class="html-italic">n</span>CeO<sub>2</sub> 25 nm suspension.</p>
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<p>Particle size distribution of <span class="html-italic">n</span>CeO<sub>2</sub> extracted after enzymatic digestion procedure from (<b>A</b>) roots and (<b>B</b>) leaves of <span class="html-italic">S. flos-cuculi</span>.</p>
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<p>Root dry mass of <span class="html-italic">S. flos cuculi</span>. Comparison of effects based on single (D1) and repeated (D2, D3) applications of 20 and 200 mg kg<sup>−1</sup> <span class="html-italic">n</span>CeO<sub>2</sub>, respectively. Letters indicate statistically significant difference between treatments (<span class="html-italic">p</span> ≤ 0.05) using one-way ANOVA followed by Tukey’s test. <sup>†</sup> One-way ANOVA <span class="html-italic">p</span>-value within each concentration: asterisks indicate the statistically significant difference of dose factor at * 0.05 ≥ <span class="html-italic">p</span> ≥ 0.01; ***<span class="html-italic">p</span> ≥ 0.001, respectively.</p>
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<p>Stem dry mass of <span class="html-italic">S. flos cuculi</span>. Comparison of effects based on single (D1) and repeated applications (D2, D3) of 20 and 200 mg kg<sup>−1</sup> <span class="html-italic">n</span>CeO<sub>2</sub>, respectively. Letters indicate statistically significant difference between treatments (<span class="html-italic">p</span> ≤ 0.05) using one-way ANOVA followed by Tukey’s test. <sup>†</sup> One-way ANOVA <span class="html-italic">p</span>-value within each concentration.</p>
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<p>Plant dry mass of <span class="html-italic">S. flos cuculi</span>. Comparison of effects based on single (D1) and repeated applications (D2, D3) of 20 and 200 mg kg<sup>−1</sup> <span class="html-italic">n</span>CeO<sub>2</sub>, respectively. Letters indicate statistically significant difference between treatments (<span class="html-italic">p</span> ≤ 0.05) using one-way ANOVA followed by Tukey’s test. <sup>†</sup> One-way ANOVA <span class="html-italic">p</span>-value within each concentration.</p>
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18 pages, 5809 KiB  
Article
Construction and Mechanism Analysis of a Self-Assembled Conductive Network in DGEBA/PEI/HRGO Nanocomposites by Controlling Filler Selective Localization
by Yiming Meng, Sushant Sharma, Wenjun Gan, Seung Hyun Hur, Won Mook Choi and Jin Suk Chung
Nanomaterials 2021, 11(1), 228; https://doi.org/10.3390/nano11010228 - 16 Jan 2021
Cited by 6 | Viewed by 3068
Abstract
Herein, a feasible and effective approach is developed to build an electrically conductive and double percolation network-like structure via the incorporation of highly reduced graphene oxide (HRGO) into a polymer blend of diglycidyl ether of bisphenol A/polyetherimide (DGEBA/PEI). With the assistance of the [...] Read more.
Herein, a feasible and effective approach is developed to build an electrically conductive and double percolation network-like structure via the incorporation of highly reduced graphene oxide (HRGO) into a polymer blend of diglycidyl ether of bisphenol A/polyetherimide (DGEBA/PEI). With the assistance of the curing reaction-induced phase separation (CRIPS) technique, an interconnected network of HRGO is formed in the phase-separated structure of the DGEBA/PEI polymer blend due to selective localization behavior. In this study, HRGO was prepared from a unique chemical reduction technique. The DGEBA/PEI/HRGO nanocomposite was analyzed in terms of phase structure by content of PEI and low weight fractions of HRGO (0.5 wt.%). The HRGO delivered a high electrical conductivity in DGEBA/PEI polyblends, wherein the value increased from 5.03 × 10−16 S/m to 5.88 S/m at a low content of HRGO (0.5 wt.%). Furthermore, the HRGO accelerated the curing reaction process of CRIPS due to its amino group. Finally, dynamic mechanical analyses (DMA) were performed to understand the CRIPS phenomenon and selective localization of HRGO reinforcement. The storage modulus increased monotonically from 1536 MPa to 1660 MPa for the 25 phr (parts per hundred in the DGEBA) PEI polyblend and reached 1915 MPa with 0.5 wt.% HRGO reinforcement. These simultaneous improvements in electrical conductivity and dynamic mechanical properties clearly demonstrate the potential of this conductive polyblend for various engineering applications. Full article
(This article belongs to the Special Issue Multifunctional Polymer-Based Nanocomposite Materials)
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<p>Schematic illustration of preparation of DGEBA/PEI/HRGO polyblend nanocomposites and the phase structure during the process.</p>
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<p>(<b>a</b>) SEM micrograph of HRGO flakes after drying, (<b>b</b>) TEM micrograph of HRGO and (<b>c</b>) Raman spectra of GO and HRGO flakes.</p>
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<p>The final phase morphologies of DGEBA/PEI/HRGO nanocomposites are (<b>a</b>) DP5H, (<b>b</b>) DP10H, (<b>c</b>) DP15H, (<b>d</b>) DP20H, (<b>e</b>) DP25H, (<b>f</b>) DP30H, and (<b>g</b>) DP30, respectively.</p>
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<p>FETEM micrographs of (<b>a</b>–<b>c</b>) DP25H polyblend from lower to higher magnification with inset in (<b>c</b>) represents HRTEM micrograph of localized HRGO at the interphase of DGEBA and PEI, and (<b>d</b>–<b>f</b>) represents DP30H polyblend with phase inversion.</p>
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<p>The electrical properties of samples for various PEI contents: (<b>a</b>) DGEBA/PEI, (<b>b</b>) DGEBA/PEI/0.5 wt.% HRGO.</p>
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<p>Schematic illustration: (<b>a</b>) structural evolution of double percolation conductive DGEBA/PEI/HRGO nanocomposites via CRIPS and (<b>b</b>) FETEM image of nanocomposite.</p>
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<p>The storage modulus versus temperature of DGEBA/PEI polyblend (<b>a</b>) at 30–230 °C and (<b>b</b>) a magnified view of the beginning of the transition (80–130 °C). Storage modulus versus temperature curves for DGEBA/PEI/HRGO nanocomposites with 0.5 wt.% HRGO at (<b>c</b>) 30–230 °C and (<b>d</b>) 80–130 °C.</p>
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<p>Tan δ versus temperature curve for DGEBA/PEI polyblend: (<b>a</b>) 30–230 °C, (<b>b</b>) 100–150 °C for T<sub>g1</sub>, (<b>c</b>) 150–230 °C for T<sub>g2</sub>, and tan δ versus temperature curve for DGEBA/PEI/HRGO nanocomposites: (<b>d</b>) 30–230 °C, (<b>e</b>) 100–150 °C for T<sub>g1</sub>, (<b>f</b>) 150–230 °C for T<sub>g2</sub>.</p>
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11 pages, 3152 KiB  
Article
Fluorescence Signal Enhancement in Antibody Microarrays Using Lightguiding Nanowires
by Damiano Verardo, Leena Liljedahl, Corinna Richter, Björn Agnarsson, Ulrika Axelsson, Christelle N. Prinz, Fredrik Höök, Carl A. K. Borrebaeck and Heiner Linke
Nanomaterials 2021, 11(1), 227; https://doi.org/10.3390/nano11010227 - 16 Jan 2021
Cited by 12 | Viewed by 3290
Abstract
Fluorescence-based detection assays play an essential role in the life sciences and medicine. To offer better detection sensitivity and lower limits of detection (LOD), there is a growing need for novel platforms with an improved readout capacity. In this context, substrates containing semiconductor [...] Read more.
Fluorescence-based detection assays play an essential role in the life sciences and medicine. To offer better detection sensitivity and lower limits of detection (LOD), there is a growing need for novel platforms with an improved readout capacity. In this context, substrates containing semiconductor nanowires may offer significant advantages, due to their proven light-emission enhancing, waveguiding properties, and increased surface area. To demonstrate and evaluate the potential of such nanowires in the context of diagnostic assays, we have in this work adopted a well-established single-chain fragment antibody-based assay, based on a protocol previously designed for biomarker detection using planar microarrays, to freestanding, SiO2-coated gallium phosphide nanowires. The assay was used for the detection of protein biomarkers in highly complex human serum at high dilution. The signal quality was quantified and compared with results obtained on conventional flat silicon and plastic substrates used in the established microarray applications. Our results show that using the nanowire-sensor platform in combination with conventional readout methods, improves the signal intensity, contrast, and signal-to-noise by more than one order of magnitude compared to flat surfaces. The results confirm the potential of lightguiding nanowires for signal enhancement and their capacity to improve the LOD of standard diagnostic assays. Full article
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<p>Scanning electron microscopy images of the GaP nanowires used in this study, taken at 30° and 0° stage inclination (perpendicular view).</p>
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<p>(<b>a</b>) Schematic representation of the single chain fragment variable (scFv) assay used in this study. ScFv antibodies (pink) are physisorbed on a surface. A blocking agent (green) is subsequently used to minimize unspecific binding of biotinylated serum proteins (blue), which are targeted by fluorescently labelled streptavidin (dark red). (<b>b</b>,<b>c</b>) Schematic representation of the assay on a flat substrate (<b>b</b>) and a light-guiding nanowire substrate (<b>c</b>): the emission of fluorophores on the nanowire surface excites the supported waveguide modes to be reemitted at the tip, leading to an enhanced signal intensity at the tip of the nanowires. (<b>d</b>–<b>f</b>) Top-view epifluorescence images (displayed in the same pixel window) of (<b>d</b>) a GaP nanowire substrate, (<b>e</b>) a silicon substrate and (<b>f</b>) a MaxiSorp black polymer substrate, spotted with antibodies and exposed biotinylated serum concentration diluted to 0.4% (the highest concentration used in this study). Individual nanowires are visible in (<b>d</b>) as bright spots. The edge of the scFv spot is visible in (<b>e</b>,<b>f</b>), showing the difference in the signal between specific an unspecific binding to the antibodies.</p>
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<p>Image analysis for signal extraction on (<b>a</b>) MaxiSorp black polymer plastic spotted with antibodies and exposed to 0.4% serum concentration, (<b>b</b>) scFv-spotted nanowires exposed to 0.4% serum concentration, and (<b>c</b>) non-spotted nanowires exposed only to 0.4% serum concentration (control sample). Panel (<b>a</b>) is displayed in a different pixel window than panels (<b>b</b>,<b>c</b>) to better show the contrast between spotted and non-spotted areas in (<b>a</b>). On flat substrates, the signal and background intensity are extracted as the mean pixel value in the areas inside (blue) and outside (red) the scFv spot, respectively. On nanowire samples, <span class="html-italic">I<sub>s</sub></span> is the mean pixel intensity on nanowire positions, (highlighted in blue in (<b>b</b>)). Similarly, <span class="html-italic">I<sub>B</sub></span> is the mean pixel intensity on nanowire positions on the control substrate (red in (<b>c</b>)).</p>
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<p>Left: extracted values of signal intensity <span class="html-italic">I<sub>s</sub></span>, Weber contrast <span class="html-italic">C<sub>W</sub></span>, and signal to noise ration (<span class="html-italic">SNR</span>) for the various scFvs on the three substrates tested with 0.4% serum concentration. All three parameters are consistently higher on the nanowire substrates. Right: example of the effect of serum concentration for the PC070 scFv. Decreasing the serum concentration results in a decrease in the signal, with 0.1% concentration approaching the limit for reliable signal on nanowires. Data for all tested scFvs are shown in the <a href="#app1-nanomaterials-11-00227" class="html-app">Figure S1</a>. Comparison graph in logarithmic scale are shown in the <a href="#app1-nanomaterials-11-00227" class="html-app">Figure S2</a>.</p>
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10 pages, 2042 KiB  
Communication
Spectral-Phase Interferometry Detection of Ochratoxin A via Aptamer-Functionalized Graphene Coated Glass
by Nikita Nekrasov, Natalya Yakunina, Averyan V. Pushkarev, Alexey V. Orlov, Ivana Gadjanski, Amaia Pesquera, Alba Centeno, Amaia Zurutuza, Petr I. Nikitin and Ivan Bobrinetskiy
Nanomaterials 2021, 11(1), 226; https://doi.org/10.3390/nano11010226 - 16 Jan 2021
Cited by 16 | Viewed by 3392
Abstract
In this work, we report a novel method of label-free detection of small molecules based on direct observation of interferometric signal change in graphene-modified glasses. The interferometric sensor chips are fabricated via a conventional wet transfer method of CVD-grown graphene onto the glass [...] Read more.
In this work, we report a novel method of label-free detection of small molecules based on direct observation of interferometric signal change in graphene-modified glasses. The interferometric sensor chips are fabricated via a conventional wet transfer method of CVD-grown graphene onto the glass coverslips, lowering the device cost and allowing for upscaling the sensor fabrication. For the first time, we report the use of graphene functionalized by the aptamer as the bioreceptor, in conjunction with Spectral-Phase Interferometry (SPI) for detection of ochratoxin A (OTA). In a direct assay with an OTA-specific aptamer, we demonstrated a quick and significant change of the optical signal in response to the maximum tolerable level of OTA concentration. The sensor regeneration is possible in urea solution. The developed platform enables a direct method of kinetic analysis of small molecules using a low-cost optical chip with a graphene-aptamer sensing layer. Full article
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<p>The sensor chip based on the glass/graphene stack. (<b>a</b>) Photography of the sensor chip. Image contrast enhancement was applied. (<b>b</b>) Raman spectra of graphene on glass. Atomic force microscopy image of graphene on glass: (<b>c</b>) height image and (<b>d</b>) phase shift contrast. Scale bar: 500 nm.</p>
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<p>(<b>a</b>) Scheme of the interference pattern formation in glass cover slip/graphene with aptamer layer on the sensing side. (<b>b</b>) Reflection spectrum of a glass cover slip with graphene on the top side.</p>
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<p>Assembling of bioreceptors on the graphene/glass stack. Sensogram showing the course of (<b>a</b>) aptamer immobilization on graphene by a chemical reaction with PBASE and (<b>b</b>) ETA deposition for deactivation of unreacted groups after aptamer deposition. Insert at (<b>a</b>): scheme of covalent bonding of an amine-modified aptamer to PBASE.</p>
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<p>Sensogram of the course of 10-nm OTA detection for pristine and aptamer-modified graphene (<b>a</b>) and data fitting to an exponential function for a time constant calculation (<b>b</b>). In (<b>a</b>), we applied an adjacent-averaging method for pristine graphene curves to decrease the noise impact.</p>
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18 pages, 6872 KiB  
Article
Comparing the Degradation Potential of Copper(II), Iron(II), Iron(III) Oxides, and Their Composite Nanoparticles in a Heterogeneous Photo-Fenton System
by Asfandyar Khan, Zsolt Valicsek and Ottó Horváth
Nanomaterials 2021, 11(1), 225; https://doi.org/10.3390/nano11010225 - 16 Jan 2021
Cited by 6 | Viewed by 3492
Abstract
Heterogeneous photo-Fenton systems offer efficient solutions for the treatment of wastewaters in the textile industry. This study investigated the fabrication and structural characterization of novel peculiar-shaped CuIIO, FeIII2O3, and FeIIO nanoparticles (NPs) compared to [...] Read more.
Heterogeneous photo-Fenton systems offer efficient solutions for the treatment of wastewaters in the textile industry. This study investigated the fabrication and structural characterization of novel peculiar-shaped CuIIO, FeIII2O3, and FeIIO nanoparticles (NPs) compared to the properties of the iron(II)-doped copper ferrite CuII0.4FeII0.6FeIII2O4. The photocatalytic efficiencies of these NPs and the composite of the simple oxides (CuIIO/FeIIO/FeIII2O3) regarding the degradation of methylene blue (MB) and rhodamine B (RhB) as model dyes were also determined. The catalysts were synthesized via simple co-precipitation and calcination technique. X-ray diffractometry (XRD), scanning electron microscopy (SEM), and diffuse reflectance spectroscopy (DRS) were utilized for structural characterization. The structure of CuIIO was bead-like connected into threads, FeIII2O3 was rod-like, while FeIIO pallet-like, with average crystallite sizes of 18.9, 36.9, and 37.1 nm, respectively. The highest degradation efficiency was achieved by CuIIO for RhB and by CuII0.4FeII0.6FeIII2O4 for MB. The CuIIO/FeIIO/FeIII2O3 composite proved to be the second-best catalyst in both cases, with excellent reusability. Hence, these NPs can be successfully applied as heterogeneous photo-Fenton catalysts for the removal of hazardous pollutants. Moreover, the simple metal oxides and the iron(II)-doped copper ferrite displayed a sufficient antibacterial activity against Gram-negative Vibrio fischeri. Full article
(This article belongs to the Special Issue Latest Developments in Photocatalytic Materials and Processes)
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Figure 1

Figure 1
<p>Flow chart representing the steps of Cu<sup>II</sup>O NPs synthesis.</p>
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<p>SEM images of synthesized metal oxide and doped ferrite nanoparticles. (<b>A</b>) Cu<sup>II</sup>O, (<b>B</b>) Fe<sup>III</sup><sub>2</sub>O<sub>3</sub>, (<b>C</b>) Fe<sup>II</sup>O, and (<b>D</b>) NP-3.</p>
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<p>Energy dispersive X-ray (EDX) spectra of simple metal oxides and doped ferrite recorded in scan mode. (<b>A</b>) Cu<sup>II</sup>O (<b>B</b>) Fe<sup>III</sup><sub>2</sub>O<sub>3</sub>, (<b>C</b>) Fe<sup>II</sup>O, and (<b>D</b>) NP-3.</p>
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<p>Comparison of the average crystallite sizes of simple metal oxides and NP-3.</p>
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<p>Comparison of band-gap energies (E<sub>bg</sub>) of the simple metal oxides and NP-3.</p>
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<p>Methylene blue degradation using doped ferrite NP-3. Experimental conditions: concentration of NP-3 = 400 mg/L, concentration of methylene blue (MB) = 1.5 × 10<sup>−5</sup> mol/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, and initial pH = 7.5.</p>
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<p>Comparison of apparent kinetic constants of Fe<sup>II</sup>O, Fe<sup>III</sup><sub>2</sub>O<sub>3</sub>, Cu<sup>II</sup>O, NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>), and Cu<sup>II</sup>O/Fe<sup>II</sup>O/Fe<sup>III</sup><sub>2</sub>O<sub>3</sub> composite. Experimental conditions: concentration of NPs = 400 mg/L, concentration of MB = 1.5 × 10<sup>−5</sup> mol/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, and initial pH = 7.5.</p>
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<p>Rhodamine B degradation using Cu<sup>II</sup>O. Experimental conditions: concentration of RhB = 1.75 × 10<sup>−5</sup> mol/L, concentration of Cu<sup>II</sup>O = 400 mg/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, and initial pH = 7.5.</p>
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<p>Comparison of apparent kinetic constants of Fe<sup>II</sup>O, Fe<sup>III</sup><sub>2</sub>O<sub>3</sub>, Cu<sup>II</sup>O, NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>), and Cu<sup>II</sup>O/Fe<sup>II</sup>O/Fe<sup>III</sup><sub>2</sub>O<sub>3</sub> composite in the photodegradation of RhB. Experimental conditions: concentration of RhB = 1.75 × 10<sup>−5</sup> mol/L, concentration of NPs = 400 mg/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, and initial pH = 7.5.</p>
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<p>(<b>A</b>) Methylene blue spectrum, and (<b>B</b>) UV-visible spectrum obtained after MB degradation using NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>). Experimental conditions: concentration of MB = 1.5 × 10<sup>−5</sup> mol/L, concentration of NPs = 400 mg/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, initial pH = 7.5, and irradiation time = 140 min.</p>
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<p>Visual representation of MB degradation in photo-Fenton process in the photo-reactor (cuvette). (<b>A</b>) Mixture of MB + NP-3 before photocatalysis, (<b>B</b>) MB + NP-3 after photocatalysis, and (<b>C</b>) clear solution obtained after separation (centrifugation) of solid catalyst from (<b>B</b>).</p>
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<p>(<b>A</b>) Rhodamine B spectrum, and (<b>B</b>) UV-visible spectrum obtained after MB degradation using NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>). Experimental conditions: concentration of NPs = 400 mg/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, concentration of RhB = 1.75 × 10<sup>−5</sup> mol/L, initial pH = 7.5, and irradiation time = 140 min.</p>
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<p>Visual representation of RhB degradation in photo-Fenton process in the photo-reactor (cuvette). (<b>A</b>) Mixture of RhB + NP-3 before photocatalysis, (<b>B</b>) RhB + NP-3 after photocatalysis, and (<b>C</b>) clear solution obtained after separation of solid catalyst from (<b>B</b>).</p>
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<p>Generalized mechanism for the degradation of organic pollutants using NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>).</p>
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<p>Comparison of bacterial inhibition percentage of Fe<sup>II</sup>O, Fe<sup>III</sup><sub>2</sub>O<sub>3</sub>, Cu<sup>II</sup>O, and doped NP-3 (Cu<sup>II</sup><sub>0.4</sub>Fe<sup>II</sup><sub>0.6</sub>Fe<sup>III</sup><sub>2</sub>O<sub>4</sub>).</p>
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<p>The effect of the reuse of Cu<sup>II</sup>O/Fe<sup>II</sup>O/Fe<sup>III</sup><sub>2</sub>O<sub>3</sub> composite catalyst on the apparent kinetic constant of MB. Experimental conditions: concentration of composite = 400 mg/L, concentration of MB = 1.5 × 10<sup>−5</sup> mol/L, concentration of H<sub>2</sub>O<sub>2</sub> = 1.76 × 10<sup>−1</sup> mol/L, pH = 7.5, and irradiation time = 140 min (each cycle).</p>
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