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Nanomaterials, Volume 10, Issue 12 (December 2020) – 252 articles

Cover Story (view full-size image): A novel magnetophotosensitizer nanoparticle (methylene blue-immobilized CuFe NP) was developed to deliver the massive reactive oxygen species into cells via the photodynamic therapy process. The nano-Cu is utilized as a template for fabricating rod-like Cu ferrite NPs. Based on the shape-assisted internalization and endogenous Fenton-like reaction, above 80% of cells are dead by treating 25 ppm of the low methylene blue-immobilized CuFe NP dose together with light-induced ^1 O_2 generation to ablate cervical cancer cells. A degradable property of rod-like CuFe NPs in the intracellular environment is promising for eliminating Cu and Fe species from the cell body. View this paper.
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12 pages, 3616 KiB  
Article
Robust Topographical Micro-Patterning of Nanofibrillar Collagen Gel by In Situ Photochemical Crosslinking-Assisted Collagen Embossing
by Hyeonjun Hong and Dong Sung Kim
Nanomaterials 2020, 10(12), 2574; https://doi.org/10.3390/nano10122574 - 21 Dec 2020
Cited by 5 | Viewed by 2990
Abstract
The topographical micro-patterning of nanofibrillar collagen gels is promising for the fabrication of biofunctional constructs mimicking topographical cell microenvironments of in vivo extracellular matrices. Nevertheless, obtaining structurally robust collagen micro-patterns through this technique is still a challenging issue. Here, we report a novel [...] Read more.
The topographical micro-patterning of nanofibrillar collagen gels is promising for the fabrication of biofunctional constructs mimicking topographical cell microenvironments of in vivo extracellular matrices. Nevertheless, obtaining structurally robust collagen micro-patterns through this technique is still a challenging issue. Here, we report a novel in situ photochemical crosslinking-assisted collagen embossing (IPC-CE) process as an integrative fabrication technique based on collagen compression-based embossing and UV–riboflavin crosslinking. The IPC-CE process using a micro-patterned polydimethylsiloxane (PDMS) master mold enables the compaction of collagen nanofibrils into micro-cavities of the mold and the simultaneous occurrence of riboflavin-mediated photochemical reactions among the nanofibrils, resulting in a robust micro-patterned collagen construct. The micro-patterned collagen construct fabricated through the IPC-CE showed a remarkable mechanical resistivity against rehydration and manual handling, which could not be achieved through the conventional collagen compression-based embossing alone. Micro-patterns of various sizes (minimum feature size <10 μm) and shapes could be obtained by controlling the compressive pressure (115 kPa) and the UV dose (3.00 J/cm2) applied during the process. NIH 3T3 cell culture on the micro-patterned collagen construct finally demonstrated its practical applicability in biological applications, showing a notable effect of anisotropic topography on cells in comparison with the conventional construct. Full article
(This article belongs to the Special Issue Development of Functional Polymer Surfaces with Nanomaterials)
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Graphical abstract
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<p>Fabrication of the in situ photochemical crosslinking-assisted collagen embossing (IPC-CE) construct. (<b>a</b>) Schematic illustration of the IPC-CE process. (<b>b</b>) Photographs of (<b>i</b>) the IPC-CE construct and (<b>ii</b>) its magnified surface. (<b>iii</b>) Manual handling of the IPC-CE construct. (<b>iv</b>) The conventional construct and (<b>v</b>) its magnified surface. (<b>vi</b>) Structural weakness of conventional construct for manual handling. White arrows in inset indicated damages induced by manual handling.</p>
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<p>Effects of processing parameters on micro-ridge patterns. Microscopic images of the IPC-CE constructs for (<b>a</b>) different compressive pressures at the same UV dose of 3.00 J/cm<sup>2</sup> and (<b>b</b>) different UV doses at same compressive pressure of 115 kPa in (<b>i</b>) rehydrated and (<b>ii</b>) dried state. All scale bars are 200 μm. (<b>c</b>) Quantitative measurement of micro-ridge pattern width for rehydrated and dried IPC-CE construct according to (<b>i</b>) compressive pressure and (<b>ii</b>) UV-dose.</p>
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<p>Microstructures of the IPC-CE constructs. SEM images of micro-ridge patterns with different widths of (<b>a</b>) 100, (<b>b</b>) 80, (<b>c</b>) 60, and (<b>d</b>) 20 μm at (<b>i</b>) low and (<b>ii</b>) high magnifications. White and black scale bars are 100 and 2 μm, respectively.</p>
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<p>Robustness and topographical effect of the IPC-CE construct. (<b>a</b>) Microscopic observation of conventional (2 and 115 kPa without UV dose) and IPC-CE construct, right after fabrication and after immersion in PBS solution. Green and yellow arrows indicate defects by partial replication and wrinkled structure, respectively. (<b>b</b>) NIH 3T3 cells cultured on each construct on day 2 (DAPI, blue; phalloidin, red). (<b>c</b>) Aspect ratio and orientation of NIH 3T3 cells. Blue arrow indicates direction of micro-ridge patterns. All scale bars are 100 μm.</p>
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17 pages, 2667 KiB  
Article
Ipriflavone-Loaded Mesoporous Nanospheres with Potential Applications for Periodontal Treatment
by Laura Casarrubios, Natividad Gómez-Cerezo, María José Feito, María Vallet-Regí, Daniel Arcos and María Teresa Portolés
Nanomaterials 2020, 10(12), 2573; https://doi.org/10.3390/nano10122573 - 21 Dec 2020
Cited by 27 | Viewed by 3009
Abstract
The incorporation and effects of hollow mesoporous nanospheres in the system SiO2–CaO (nanoMBGs) containing ipriflavone (IP), a synthetic isoflavone that prevents osteoporosis, were evaluated. Due to their superior porosity and capability to host drugs, these nanoparticles are designed as a potential [...] Read more.
The incorporation and effects of hollow mesoporous nanospheres in the system SiO2–CaO (nanoMBGs) containing ipriflavone (IP), a synthetic isoflavone that prevents osteoporosis, were evaluated. Due to their superior porosity and capability to host drugs, these nanoparticles are designed as a potential alternative to conventional bioactive glasses for the treatment of periodontal defects. To identify the endocytic mechanisms by which these nanospheres are incorporated within the MC3T3-E1 cells, five inhibitors (cytochalasin B, cytochalasin D, chlorpromazine, genistein and wortmannin) were used before the addition of these nanoparticles labeled with fluorescein isothiocyanate (FITC–nanoMBGs). The results indicate that nanoMBGs enter the pre-osteoblasts mainly through clathrin-dependent mechanisms and in a lower proportion by macropinocytosis. The present study evidences the active incorporation of nanoMBG–IPs by MC3T3-E1 osteoprogenitor cells that stimulate their differentiation into mature osteoblast phenotype with increased alkaline phosphatase activity. The final aim of this study is to demonstrate the biocompatibility and osteogenic behavior of IP-loaded bioactive nanoparticles to be used for periodontal augmentation purposes and to shed light on internalization mechanisms that determine the incorporation of these nanoparticles into the cells. Full article
(This article belongs to the Special Issue Nano-Engineering Solutions for Dental Implant Applications)
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Figure 1
<p>Characterization of mesoporous nanospheres. (<b>a</b>) scanning electron micrograph of hollow mesoporous nanospheres in the system SiO<sub>2</sub>–CaO (nanoMBG) spheres. (<b>b</b>) Transmission electron image of nanoMBG spheres. (<b>c</b>) Nitrogen adsorption/desorption isotherm of nanoMBG spheres. (<b>d</b>) FTIR spectra of nanoMBG and IP-loaded nanospheres (nanoMBG–IP) spheres (* indicates the absorption bands corresponding to ipriflavone).</p>
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<p>Effects of nanoMBGs and nanoMBG–IPs on cell cycle phases of MC3T3-E1 pre-osteoblasts and apoptosis percentage (Sub G<sub>1</sub> fraction) after 24 h of treatment with 50 μg/mL of nanospheres. Control conditions without nanospheres were performed at the same time. Statistical significance: *** <span class="html-italic">p</span> &lt; 0.005.</p>
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<p>Effects of 50 μg/mL of nanoMBG and nanoMBG–IP nanospheres on viability, intracellular content of reactive oxygen species (ROS) and cytosolic calcium of MC3T3-E1 pre-osteoblasts, after 24 h of incubation. Control conditions without nanospheres were performed at the same time. Fluorescence profiles of control cells, cells with Fluo4 and cells with Fluo4 plus A23187 ionophore are shown in the lower-left figure. Statistical significance: *** <span class="html-italic">p</span> &lt; 0.005.</p>
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<p>Effects of several doses of nanoMBGs and nanoMBG–IPs on MC3T3-E1 pre-osteoblast differentiation after 11 days, evaluated through the measurement of alkaline phosphatase (ALP) activity. Control conditions without nanospheres were performed at the same time. Statistical significance: *** <span class="html-italic">p</span> &lt; 0.005, * <span class="html-italic">p</span> &lt; 0.05.</p>
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<p>Effects of nanoMBGs and nanoMBG–IPs on interleukin 6 (IL-6) production by cultured MC3T3-E1 pre-osteoblasts after treatment with 50 μg/mL of nanospheres for 24 h. Control conditions without nanospheres were performed at the same time.</p>
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<p>Intracellular uptake of nanoMBG nanospheres labeled with FITC by MC3T3-E1 pre-osteoblasts. (<b>A</b>) flow cytometric analysis of fluorescence intensity of cells with intracellular FITC–nanoMBG nanospheres after incubation with 10 (●), 30 (○) and 50 µg/mL (▼) for different times (15, 30 and 60 min). Statistical significance: *** <span class="html-italic">p</span> &lt; 0.005. (<b>B</b>) Confocal microscopy images of MC3T3-E1 pre-osteoblasts after 24 h of incubation with 50 μg/mL of nanoMBG nanospheres labeled with fluorescein isothiocyanate (FITC). Nuclei were stained with DAPI (blue), F-actin filaments were stained with rhodamine-phalloidin (red), and FITC–nanoMBGs are observed in green.</p>
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<p>Inhibitory effects of several endocytosis inhibitors on FITC–nanoMBG uptake by MC3T3-E1 pre-osteoblasts. Cells were incubated with each inhibitor for 2 h, the medium was then removed, and the cultures were treated with 50 µg/mL FITC–nanoMBGs for 2 h. Statistical significance: * <span class="html-italic">p</span> &lt; 0.05, *** <span class="html-italic">p</span> &lt; 0.005.</p>
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10 pages, 2208 KiB  
Article
Photocatalytic Overall Water Splitting by SrTiO3 with Surface Oxygen Vacancies
by Yanfei Fan, Yan Liu, Hongyu Cui, Wen Wang, Qiaoyan Shang, Xifeng Shi, Guanwei Cui and Bo Tang
Nanomaterials 2020, 10(12), 2572; https://doi.org/10.3390/nano10122572 - 21 Dec 2020
Cited by 38 | Viewed by 4782
Abstract
Strontium Titanate has a typical perovskite structure with advantages of low cost and photochemical stability. However, the wide bandgap and rapid recombination of electrons and holes limited its application in photocatalysis. In this work, a SrTiO3 material with surface oxygen vacancies was [...] Read more.
Strontium Titanate has a typical perovskite structure with advantages of low cost and photochemical stability. However, the wide bandgap and rapid recombination of electrons and holes limited its application in photocatalysis. In this work, a SrTiO3 material with surface oxygen vacancies was synthesized via carbon reduction under a high temperature. It was successfully applied for photocatalytic overall water splitting to produce clean hydrogen energy under visible light irradiation without any sacrificial reagent for the first time. The photocatalytic overall water splitting ability of the as-prepared SrTiO3-C950 is attributed to the surface oxygen vacancies that can make suitable energy levels for visible light response, improving the separation and transfer efficiency of photogenerated carriers. Full article
(This article belongs to the Section Energy and Catalysis)
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Figure 1
<p>Morphology and Structure characterizations of SrTiO<sub>3</sub>. (<b>a</b>), Scanning Electron Microscope (SEM) image of SrTiO<sub>3</sub>; (<b>b</b>), SEM of SrTiO<sub>3</sub>-C950; (<b>c</b>), XRD of SrTiO<sub>3</sub> and SrTiO<sub>3</sub>-C950.</p>
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<p>Transmission Electron Microscope (TEM) image (<b>a</b>), High Resolution Transmission Electron Microscope (HRTEM) image (<b>b</b>) and Electron Paramagnetic Resonance (EPR) image (<b>c</b>) of SrTiO<sub>3</sub>-C950.</p>
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<p>XPS spectra of Sr3d (<b>a</b>), O1s (<b>b</b>), Ti2p (<b>c</b>) and C1s (<b>d</b>) of SrTiO<sub>3</sub> and SrTiO<sub>3</sub>-C950.</p>
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<p>Photocatalytic activity of SrTiO<sub>3</sub>-C950 under full-spectrum light irradiation (<b>a</b>) or visible light irradiation (<b>b</b>) without sacrificial reagent. No photocatalytic water splitting activity was observed for pristine SrTiO<sub>3</sub> and SrTiO<sub>3</sub>-C300 under the same conditions.</p>
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<p>Ultraviolet–visible diffuse reflectance spectrum (UV-Vis DRS) (<b>a</b>), XPS Valence Band Spectrum and Energy band structure of SrTiO<sub>3</sub> (left) and SrTiO<sub>3</sub>-C950 (right) (<b>b</b>), Electrochemical impedance spectroscopy (<b>c</b>) and Photocurrent density (<b>d</b>) of SrTiO<sub>3</sub>-C950 and SrTiO<sub>3</sub>.</p>
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26 pages, 4899 KiB  
Review
A Guided Walk through the World of Mesoporous Bioactive Glasses (MBGs): Fundamentals, Processing, and Applications
by Carla Migneco, Elisa Fiume, Enrica Verné and Francesco Baino
Nanomaterials 2020, 10(12), 2571; https://doi.org/10.3390/nano10122571 - 21 Dec 2020
Cited by 55 | Viewed by 5241
Abstract
Bioactive glasses (BGs) are traditionally known to be able to bond to living bone and stimulate bone regeneration. The production of such materials in a mesoporous form allowed scientists to dramatically expand the versatility of oxide-based glass systems as well as their applications [...] Read more.
Bioactive glasses (BGs) are traditionally known to be able to bond to living bone and stimulate bone regeneration. The production of such materials in a mesoporous form allowed scientists to dramatically expand the versatility of oxide-based glass systems as well as their applications in biomedicine. These nanostructured materials, called mesoporous bioactive glasses (MBGs), not only exhibit an ultrafast mineralization rate but can be used as vehicles for the sustained delivery of drugs, which are hosted inside the mesopores, and therapeutic ions, which are released during material dissolution in contact with biological fluids. This review paper summarizes the main strategies for the preparation of MBGs, as well as their properties and applications in the biomedical field, with an emphasis on the methodological aspects and the promise of hierarchical systems with multiscale porosity. Full article
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<p>Summary of mesoporous bioactive glass (MBG) properties that make these materials highly attractive for biotechnological and biomedical applications [<a href="#B20-nanomaterials-10-02571" class="html-bibr">20</a>].</p>
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<p>Production of MBGs by the so-called “wet” method. The image shows a gel-derived glass (<b>left side</b>) and mesoporous silica (<b>right side</b>) obtained by sol–gel and supramolecular arrangement routes, respectively. MBGs are produced by combining these two routes (middle image) [<a href="#B27-nanomaterials-10-02571" class="html-bibr">27</a>].</p>
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<p>Phase sequence of a water–surfactant binary system following surfactant concentration [<a href="#B12-nanomaterials-10-02571" class="html-bibr">12</a>].</p>
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<p>Ternary phase diagram of P123–water–ethanol system at <span class="html-italic">T</span> = 23 °C. L1 denotes the region with isotropic solution (water-rich), I1 refers to isotropic gels, H1 refers to cylindrical micelles arranged in a 2D hexagonal lattice, and Lα is the lamellar phase. The region boundaries are traced by solid lines [<a href="#B39-nanomaterials-10-02571" class="html-bibr">39</a>].</p>
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<p>Ternary phase diagram of F127–water–buthanol system. L1 denotes the region with isotropic solution (water-rich), I1 refers to isotropic gels, H1 refers to cylindrical micelles arranged in a 2D hexagonal lattice, Lα is the lamellar phase, and L2 is a reverse isotropic micellar phase. The region boundaries are traced by solid lines. The arrow indicates the delicate balance of these regions: for example, the rapid evaporation of solvent may occur during some processes, such as spin-coating, thereby producing a transition from lamellar to hexagonal phase [<a href="#B38-nanomaterials-10-02571" class="html-bibr">38</a>].</p>
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<p>Stages of the evaporation-induced self-assembly (EISA) process for the production of MBGs. Image adapted from [<a href="#B14-nanomaterials-10-02571" class="html-bibr">14</a>].</p>
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<p>Transmission electron microscopy images of (<b>a</b>) P123-templated MBG and (<b>b</b>) cetyltrimethylammonium bromide (CTAB)-templated MBG [<a href="#B7-nanomaterials-10-02571" class="html-bibr">7</a>].</p>
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<p>Typical TEM images of F127-induced MBGs (<b>a</b>), in which the pore and wall structures are indicated by white lines in (<b>b</b>) [<a href="#B49-nanomaterials-10-02571" class="html-bibr">49</a>].</p>
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<p>High-resolution transmission electron microscopy images and electron diffraction patterns of conventional sol–gel SiO<sub>2</sub>–CaO–P<sub>2</sub>O<sub>5</sub> glasses, SiO<sub>2</sub>–CaO–P<sub>2</sub>O<sub>5</sub> MBG, and pure mesoporous silica [<a href="#B42-nanomaterials-10-02571" class="html-bibr">42</a>].</p>
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<p>Nano-crystalline apatite mineralization on the surface of three-dimensional MBG scaffolds: (<b>a</b>) “cauliflower” globular agglomerates (low magnification image), (<b>b</b>) details of nano-crystals (high magnification image) [<a href="#B7-nanomaterials-10-02571" class="html-bibr">7</a>].</p>
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<p>Schematic concept of using MBGs for drug delivery and bone regeneration [<a href="#B70-nanomaterials-10-02571" class="html-bibr">70</a>].</p>
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<p>Photographs of (<b>a</b>) the polyurethane sponges used as macroporous templates and (<b>b</b>) the resulting hierarchical MBG scaffolds [<a href="#B56-nanomaterials-10-02571" class="html-bibr">56</a>].</p>
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<p>SEM analysis of polyurethane sponges (<b>a</b>,<b>b</b>) and macro-mesoporous scaffolds with composition (mol.%) 100SiO<sub>2</sub> (<b>c</b>,<b>d</b>), 90SiO<sub>2</sub>–5CaO–5P<sub>2</sub>O<sub>5</sub> (<b>e</b>,<b>f</b>), 80SiO<sub>2</sub>–15CaO–5P<sub>2</sub>O<sub>5</sub> (<b>g</b>,<b>h</b>), and 70SiO<sub>2</sub>–25CaO–5P<sub>2</sub>O<sub>5</sub> (<b>i</b>,<b>j</b>) [<a href="#B56-nanomaterials-10-02571" class="html-bibr">56</a>].</p>
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14 pages, 2591 KiB  
Article
Temperature-Dependent Photoluminescent Properties of PbSe Nanoplatelets
by Ivan Skurlov, Anastasiia Sokolova, Tom Galle, Sergei Cherevkov, Elena Ushakova, Alexander Baranov, Vladimir Lesnyak, Anatoly Fedorov and Aleksandr Litvin
Nanomaterials 2020, 10(12), 2570; https://doi.org/10.3390/nano10122570 - 21 Dec 2020
Cited by 14 | Viewed by 4672
Abstract
Semiconductor colloidal nanoplatelets (NPLs) are a promising new class of nanostructures that can bring much impact on lightning technologies, light-emitting diodes (LED), and laser fabrication. Indeed, great progress has been made in optimizing the optical properties of the NPLs for the visible spectral [...] Read more.
Semiconductor colloidal nanoplatelets (NPLs) are a promising new class of nanostructures that can bring much impact on lightning technologies, light-emitting diodes (LED), and laser fabrication. Indeed, great progress has been made in optimizing the optical properties of the NPLs for the visible spectral range, which has already made the implementation of a number of effective devices on their basis possible. To date, state-of-the-art near-infrared (NIR)-emitting NPLs are significantly inferior to their visible-range counterparts, although it would be fair to say that they received significantly less research attention so far. In this study, we report a comprehensive analysis of steady-state and time-dependent photoluminescence (PL) properties of four monolayered (ML) PbSe NPLs. The PL measurements are performed in a temperature range of 78–300 K, and their results are compared to those obtained for CdSe NPLs and PbSe quantum dots (QDs). We show that multiple emissive states, both band-edge and trap-related, are responsible for the formation of the NPLs’ PL band. We demonstrate that the widening of the PL band is caused by the inhomogeneous broadening rather than homogeneous one, and analyze the possible contributions to PL broadening. Full article
(This article belongs to the Special Issue Electronic and Optical Properties of Nanostructures)
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Graphical abstract
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<p>(<b>A</b>) Absorption (black line) and photoluminescence (PL) (red dots) spectra of four monolayered (ML) PbSe nanoplatelets (NPLs) in tetrachloroethylene; (<b>B</b>) transmission electron microscopy (TEM) image of 4 ML PbSe NPLs (<b>C</b>) PL decay curves recorded at different temperatures, inset—PL spectra obtained in 78–300 K temperature range (<b>D</b>) averaged PL decay times vs. temperature, inset—integrated PL intensity vs. temperature.</p>
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<p>PL spectra of 4 ML PbSe NPLs at (<b>A</b>) 295 K and (<b>B</b>) 78 K, green line stays for PL1, red line—for PL2; (<b>C</b>) energy splitting between PL1 and PL2 peak positions; (<b>D</b>) ratio of PL2 to PL1 areas, black dots—NPLs purified in inert atmosphere, red dots—NPLs purified in ambient atmosphere.</p>
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<p>(<b>A</b>) PL1 peak position of four ML PbSe NPLs vs. temperature, the red line marks the Varshni fit, the green line marks the O’Donnel-Chen fit, and the semi-transparent areas mark the 95% confidence band; (<b>B</b>) PL1 full width at half maximum (FWHM) vs. temperature, lines show the FWHM fit with Equation (3) (red) and Equation (4) (green), and the semi-transparent areas mark the 95% confidence band; (<b>C</b>,<b>D</b>) PbSe (purple) and (<b>E</b>,<b>F</b>) CdSe (red) Gaussian (solid), and Lorentz (open) linewidths extracted from the Voight fitting.</p>
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24 pages, 3778 KiB  
Review
Recent Developments in Lead and Lead-Free Halide Perovskite Nanostructures towards Photocatalytic CO2 Reduction
by Chaitanya B. Hiragond, Niket S. Powar and Su-Il In
Nanomaterials 2020, 10(12), 2569; https://doi.org/10.3390/nano10122569 - 21 Dec 2020
Cited by 47 | Viewed by 6436
Abstract
Perovskite materials have been widely considered as emerging photocatalysts for CO2 reduction due to their extraordinary physicochemical and optical properties. Perovskites offer a wide range of benefits compared to conventional semiconductors, including tunable bandgap, high surface energy, high charge carrier lifetime, and [...] Read more.
Perovskite materials have been widely considered as emerging photocatalysts for CO2 reduction due to their extraordinary physicochemical and optical properties. Perovskites offer a wide range of benefits compared to conventional semiconductors, including tunable bandgap, high surface energy, high charge carrier lifetime, and flexible crystal structure, making them ideal for high-performance photocatalytic CO2 reduction. Notably, defect-induced perovskites, for example, crystallographic defects in perovskites, have given excellent opportunities to tune perovskites’ catalytic properties. Recently, lead (Pb) halide perovskite and their composites or heterojunction with other semiconductors, metal nanoparticles (NPs), metal complexes, graphene, and metal-organic frameworks (MOFs) have been well established for CO2 conversion. Besides, various halide perovskites have come under focus to avoid the toxicity of lead-based materials. Therefore, we reviewed the recent progress made by Pb and Pb-free halide perovskites in photo-assisted CO2 reduction into useful chemicals. We also discussed the importance of various factors like change in solvent, structure defects, and compositions in the fabrication of halide perovskites to efficiently convert CO2 into value-added products. Full article
(This article belongs to the Special Issue Nanomaterials toward CO2 Reduction and Conversion)
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<p>(<b>a–d</b>) CsPbBr<sub>3</sub> quantum dots (QDs) TEM images showing the difference in particle size, (<b>e</b>) photocatalytic CO<sub>2</sub> reduction using an optimized sample of CsPbBr<sub>3</sub>, (<b>f</b>) particle size effect on the CO<sub>2</sub> reduction activity, (<b>g</b>) Time-resolved photoluminescence (TRPL) decay of different samples, and (<b>h</b>) band diagram showing mechanism of CO<sub>2</sub> reduction to chemical fuels. Reproduced from [<a href="#B61-nanomaterials-10-02569" class="html-bibr">61</a>], with permission from John Wiley and Sons, 2017.</p>
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<p>The free energy diagram showing the pathway of CO<sub>2</sub> reduction on pristine and Co/Fe doped CsPbBr<sub>3</sub>. Reproduced from [<a href="#B63-nanomaterials-10-02569" class="html-bibr">63</a>], Royal Society of Chemistry, 2019.</p>
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<p>The comparative (<b>a</b>) PL spectra, (<b>b</b>) PL decay, (<b>c</b>) transient absorption kinetic plots (at an excitation wavelength of 400 nm) among CsPbBr<sub>3</sub> NC and composite samples, (<b>d</b>) schematic illustration and band alignment of CsPbBr<sub>3</sub>/Pd composite for CO<sub>2</sub> reduction, (<b>e</b>) photocatalytic CO<sub>2</sub> reduction performance, and (<b>f</b>) quantum efficiency of different samples. Reproduced from [<a href="#B76-nanomaterials-10-02569" class="html-bibr">76</a>], with permission from Royal Society of Chemistry, 2019.</p>
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<p>(<b>a</b>) An in−situ synthetic procedure for CsPbBr<sub>3</sub>/MXene, (<b>b</b>−<b>d</b>) TEM and HR-TEM images of CsPbBr<sub>3</sub>/MXene-20 composite and (<b>e</b>−<b>i</b>) EDX elemental mapping for the respective elements. Reproduced from [<a href="#B77-nanomaterials-10-02569" class="html-bibr">77</a>], with permission from American Chemical Society, 2019.</p>
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<p>(<b>a</b>−<b>c</b>) Ex-situ and in-situ XPS of TiO<sub>2</sub> (T) and TiO<sub>2</sub>/CsPbBr<sub>3</sub> (TC2) samples (TC2-UV is in-situ XPS under UV light irradiation), and electrostatic potentials for (<b>d</b>) anatase TiO<sub>2</sub> (101), (<b>e</b>) rutile TiO<sub>2</sub> (110) and (<b>f</b>) CsPbBr<sub>3</sub> (001) facets. Reproduced from [<a href="#B79-nanomaterials-10-02569" class="html-bibr">79</a>], with permission from Springer Nature, 2020.</p>
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<p>(<b>a</b>) Schematic illustration of synthesis and utilization of CsPbBr<sub>3</sub>/ZIFs for CO<sub>2</sub> reduction, (<b>b</b>,<b>c</b>) TEM of CsPbBr<sub>3</sub>@ZIF-8, (<b>d</b>) HAADF-STEM of CsPbBr<sub>3</sub>@ZIF-27, (<b>e</b>) TEM of CsPbBr<sub>3</sub>@ZIF-27, (<b>f</b>) CO<sub>2</sub> reduction results for pristine and composite, and (<b>g</b>) Stability test for CsPbBr<sub>3</sub>@ZIF-67. Reproduced from [<a href="#B85-nanomaterials-10-02569" class="html-bibr">85</a>], with permission from American chemical society, 2018.</p>
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<p>(<b>a</b><b>,b</b>) The XRD patterns, (<b>c</b>) UV-Vis/PL spectra and (<b>d</b>,<b>e</b>) TEM images of FAPbBr<sub>3</sub>, and CsPbBr<sub>3</sub>, (<b>f</b>) Results of comparative photocatalytic CO<sub>2</sub> reduction in FAPbBr<sub>3</sub> and CsPbBr<sub>3</sub>, and (<b>g</b>) reusability test of FAPbBr<sub>3</sub>. Reproduced from [<a href="#B94-nanomaterials-10-02569" class="html-bibr">94</a>], with permission from Elsevier, 2020.</p>
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<p>(<b>a</b>) XPS, (<b>b</b>) FTIR, and (<b>c</b>,<b>d</b>) TGA analysis of Cs<sub>2</sub>AgBiBr<sub>6</sub> before and after the washing. Reproduced from [<a href="#B104-nanomaterials-10-02569" class="html-bibr">104</a>], with permission from John Wiley and Sons, 2018.</p>
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<p>(<b>a</b>) CO and CH<sub>4</sub> formation, (<b>b</b>) times course product formation in different samples of Cs<sub>2</sub>AgBiBr<sub>6</sub>, and (<b>c</b>) Schematic illustration of CO<sub>2</sub> reduction on the surface of Cs<sub>2</sub>AgBiBr<sub>6</sub>. Reproduced from [<a href="#B104-nanomaterials-10-02569" class="html-bibr">104</a>], with permission from John Wiley and Sons, 2018.</p>
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<p>(<b>a</b>) Schematic illustration of the synthesis of Bi−based perovskites by top-down method, (<b>b</b>) Time−dependent CH<sub>4</sub> production in Bi−based perovskites, and (<b>c</b>) yields of CO and CH<sub>4</sub> production in different samples. Reproduced from [<a href="#B107-nanomaterials-10-02569" class="html-bibr">107</a>], with permission from American Chemical Society, 2019.</p>
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10 pages, 6287 KiB  
Article
Van der Waals Integrated Silicon/Graphene/AlGaN Based Vertical Heterostructured Hot Electron Light Emitting Diodes
by Nallappagari Krishnamurthy Manjunath, Chang Liu, Yanghua Lu, Xutao Yu and Shisheng Lin
Nanomaterials 2020, 10(12), 2568; https://doi.org/10.3390/nano10122568 - 21 Dec 2020
Cited by 1 | Viewed by 2656
Abstract
Silicon-based light emitting diodes (LED) are indispensable elements for the rapidly growing field of silicon compatible photonic integration platforms. In the present study, graphene has been utilized as an interfacial layer to realize a unique illumination mechanism for the silicon-based LEDs. We designed [...] Read more.
Silicon-based light emitting diodes (LED) are indispensable elements for the rapidly growing field of silicon compatible photonic integration platforms. In the present study, graphene has been utilized as an interfacial layer to realize a unique illumination mechanism for the silicon-based LEDs. We designed a Si/thick dielectric layer/graphene/AlGaN heterostructured LED via the van der Waals integration method. In forward bias, the Si/thick dielectric (HfO2-50 nm or SiO2-90 nm) heterostructure accumulates numerous hot electrons at the interface. At sufficient operational voltages, the hot electrons from the interface of the Si/dielectric can cross the thick dielectric barrier via the electron-impact ionization mechanism, which results in the emission of more electrons that can be injected into graphene. The injected hot electrons in graphene can ignite the multiplication exciton effect, and the created electrons can transfer into p-type AlGaN and recombine with holes resulting a broadband yellow-color electroluminescence (EL) with a center peak at 580 nm. In comparison, the n-Si/thick dielectric/p-AlGaN LED without graphene result in a negligible blue color EL at 430 nm in forward bias. This work demonstrates the key role of graphene as a hot electron active layer that enables the intense EL from silicon-based compound semiconductor LEDs. Such a simple LED structure may find applications in silicon compatible electronics and optoelectronics. Full article
(This article belongs to the Special Issue State-of-the-Art Optoelectronic and Electronic Nanodevices in China)
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<p>(<b>a</b>) Cross-sectional high-resolution Transmission Electron Microscope (HR-TEM) image of the interface of n-Si/HfO<sub>2</sub> heterostructure. (<b>a<sub>1</sub></b>) Transmission Electron Microscope (TEM) image of cross-sectional view of the interface of n-Si/HfO<sub>2</sub> with 100 nm scale. (<b>a<sub>2</sub></b>) and (<b>a<sub>3</sub></b>) TEM magnified view of the interface of n-Si/HfO<sub>2</sub>, from which a thickness of 54.5 nm for the HfO<sub>2</sub> layer, SiO<sub>2</sub> interface layer, and a hetero-layered stacking of Si and HfO<sub>2</sub> can be read out respectively. (<b>b</b>) STEM-EDX elemental mapping of (<b>b<sub>1</sub></b>) Si, (<b>b<sub>2</sub></b>) Hf, (<b>b<sub>3</sub></b>) Pt, and (<b>b<sub>4</sub></b>) O in the hetero-layered structure of n-Si/HfO<sub>2</sub>.</p>
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<p>(<b>a</b>) Pictorial view of the graphene free n-Si/HfO<sub>2</sub>/p-AlGaN LED. (<b>b</b>) Current-Voltage (I–V) characteristic curve of the LED. (<b>c</b>) Electroluminescence (EL) of the LED at forward bias applied voltages.</p>
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<p>(<b>a</b>) Structure of n-Si/HfO<sub>2</sub>/DLG/p-AlGaN LED. (<b>b</b>) Current-Voltage (I–V) characteristics of the LED. (<b>c</b>) Electroluminescence (EL) of the LED at applied forward bias voltages. Defects based broadband yellow color with peak center at 580 nm.</p>
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<p>(<b>a</b>) Energy band profile of n-Si/HfO<sub>2</sub>/DLG/p-AlGaN vertical semiconductor heterostructure under zero bias condition. (<b>b</b>) The illumination mechanism of the LED at forward bias voltages. (<b>c</b>) Pictorial view of the electronic band profile of graphene in the LED at zero bias. (<b>d</b>) Pictorial view of the band profile of graphene in the LED at forward bias. Electric field induced hot electron accumulation at the graphene led to the n-type doped graphene and rise in Fermi level of the graphene.</p>
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<p>(<b>a</b>) Schematic representation of the structure of graphene free n-Si/SiO<sub>2</sub>/p-AlGaN LED. (<b>b</b>) Current-Voltage (I–V) curve of the graphene free LED. (<b>c</b>) Electroluminescence (EL) of the graphene free LED at forward bias applied voltages. (<b>d</b>) Pictorial view of the graphene based Si/SiO<sub>2</sub>/DLG/AlGaN LED. (<b>e</b>) I–V curve of the graphene based LED. (<b>f</b>) EL from the graphene based LED in forward bias. The illumination from the graphene based LED was a defect based broadband yellow color with a wavelength maxima (λ<sub>max</sub>) at 580 nm.</p>
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20 pages, 3406 KiB  
Review
Biodegradable Poly(Lactic Acid) Nanocomposites for Fused Deposition Modeling 3D Printing
by Madison Bardot and Michael D. Schulz
Nanomaterials 2020, 10(12), 2567; https://doi.org/10.3390/nano10122567 - 21 Dec 2020
Cited by 71 | Viewed by 7905
Abstract
3D printing by fused deposition modelling (FDM) enables rapid prototyping and fabrication of parts with complex geometries. Unfortunately, most materials suitable for FDM 3D printing are non-degradable, petroleum-based polymers. The current ecological crisis caused by plastic waste has produced great interest in biodegradable [...] Read more.
3D printing by fused deposition modelling (FDM) enables rapid prototyping and fabrication of parts with complex geometries. Unfortunately, most materials suitable for FDM 3D printing are non-degradable, petroleum-based polymers. The current ecological crisis caused by plastic waste has produced great interest in biodegradable materials for many applications, including 3D printing. Poly(lactic acid) (PLA), in particular, has been extensively investigated for FDM applications. However, most biodegradable polymers, including PLA, have insufficient mechanical properties for many applications. One approach to overcoming this challenge is to introduce additives that enhance the mechanical properties of PLA while maintaining FDM 3D printability. This review focuses on PLA-based nanocomposites with cellulose, metal-based nanoparticles, continuous fibers, carbon-based nanoparticles, or other additives. These additives impact both the physical properties and printability of the resulting nanocomposites. We also detail the optimal conditions for using these materials in FDM 3D printing. These approaches demonstrate the promise of developing nanocomposites that are both biodegradable and mechanically robust. Full article
(This article belongs to the Special Issue Functional Biodegradable Nanocomposites)
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<p>Poly(lactic acid) conformers.</p>
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<p>(<b>a</b>) Flat, on-edge, and up right printing orientation of tensile bars. (<b>b</b>) Processing parameters of tensile bars. Reproduced with permission from [<a href="#B27-nanomaterials-10-02567" class="html-bibr">27</a>], Elseveir, 2017.</p>
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<p>Cellulose chemical structure.</p>
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<p>Depiction of rotation and crosshatched 3D printing pattern utilized to increase mechanical properties of 3D-printed materials. Reproduced with permission from [<a href="#B44-nanomaterials-10-02567" class="html-bibr">44</a>], Wiley, 2020.</p>
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<p>Poly(lactic acid) (PLA)/copper fiber surfaces (<b>A</b>,<b>B</b>) before laser treatment showing gaps, voids, and uneven surface morphology and (<b>C</b>) after 5 W laser treatment with a 175 µm beam. Reproduced with permission from [<a href="#B49-nanomaterials-10-02567" class="html-bibr">49</a>], Wiley, 2020.</p>
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<p>Compatibilized magnesium nanoparticle PLA filaments. (<b>A</b>) Fused deposition modelling (FDM) 3D-printed scaffold, (<b>B</b>) layer structure of scaffold, (<b>C</b>) cross section of individual layer showing magnesium dispersion. Reproduced with permission from [<a href="#B53-nanomaterials-10-02567" class="html-bibr">53</a>], Elsevier, 2020.</p>
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<p>FDM 3D printing apparatus with continuous fibers. Reproduced with permission from [<a href="#B63-nanomaterials-10-02567" class="html-bibr">63</a>], Elsevier, 2016.</p>
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<p>Depiction of fibers in FDM 3D-printed material and the different defects that occur with stress including fiber pull-out, filament delamination, debonding, and fiber breakage. Reproduced with permission from [<a href="#B49-nanomaterials-10-02567" class="html-bibr">49</a>], Wiley, 2020.</p>
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<p>Integration of graphene nanoparticles into FDM 3D-printed PLA. (<b>a</b>) Neat PLA after FDM 3D printing. (<b>b</b>) PLA/graphene nanocomposite after FDM 3D printing. (<b>c</b>) PLA and (<b>d</b>) PLA/graphene fractured cross-sectional microstructure. Reproduced with permission from [<a href="#B82-nanomaterials-10-02567" class="html-bibr">82</a>], Wiley, 2018.</p>
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18 pages, 29842 KiB  
Article
Graphene Quantum Dot-TiO2 Photonic Crystal Films for Photocatalytic Applications
by Maria-Athina Apostolaki, Alexia Toumazatou, Maria Antoniadou, Elias Sakellis, Evangelia Xenogiannopoulou, Spiros Gardelis, Nikos Boukos, Polycarpos Falaras, Athanasios Dimoulas and Vlassis Likodimos
Nanomaterials 2020, 10(12), 2566; https://doi.org/10.3390/nano10122566 - 21 Dec 2020
Cited by 16 | Viewed by 3935
Abstract
Photonic crystal structuring has emerged as an advanced method to enhance solar light harvesting by metal oxide photocatalysts along with rational compositional modifications of the materials’ properties. In this work, surface functionalization of TiO2 photonic crystals by blue luminescent graphene quantum dots [...] Read more.
Photonic crystal structuring has emerged as an advanced method to enhance solar light harvesting by metal oxide photocatalysts along with rational compositional modifications of the materials’ properties. In this work, surface functionalization of TiO2 photonic crystals by blue luminescent graphene quantum dots (GQDs), n–π* band at ca. 350 nm, is demonstrated as a facile, environmental benign method to promote photocatalytic activity by the combination of slow photon-assisted light trapping with GQD-TiO2 interfacial electron transfer. TiO2 inverse opal films fabricated by the co-assembly of polymer colloidal spheres with a hydrolyzed titania precursor were post-modified by impregnation in aqueous GQDs suspension without any structural distortion. Photonic band gap engineering by varying the inverse opal macropore size resulted in selective performance enhancement for both salicylic acid photocatalytic degradation and photocurrent generation under UV–VIS and visible light, when red-edge slow photons overlapped with the composite’s absorption edge, whereas stop band reflection was attenuated by the strong UVA absorbance of the GQD-TiO2 photonic films. Photoelectrochemical and photoluminescence measurements indicated that the observed improvement, which surpassed similarly modified benchmark mesoporous P25 TiO2 films, was further assisted by GQDs electron acceptor action and visible light activation to a lesser extent, leading to highly efficient photocatalytic films. Full article
(This article belongs to the Section 2D and Carbon Nanomaterials)
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<p>Top-view SEM images of (<b>a</b>) PC211, (<b>b</b>) PC261, (<b>c</b>) PC300, (<b>d</b>) PC340, (<b>e</b>) GQD-PC211 inverse opals, and (<b>f</b>) cross-section image of PC340. Top-view (<b>g</b>) and cross-section (<b>h</b>) images of P25 films.</p>
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<p>Specular reflectance (R%) spectra for the (<b>a</b>) PC211, (<b>b</b>) PC261, (<b>c</b>) PC300, and (<b>d</b>) PC340 photonic films before and after QGDs surface modification at 15° incidence angle.</p>
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<p>(<b>a</b>) Absorbance and photoluminescence (PL) of the graphene quantum dot (GQD) suspension (diluted to 0.025 mg/mL). Diffuse (DR%) reflectance spectra for (<b>b</b>) PC211, (<b>c</b>) PC261, (<b>d</b>) PC300, (<b>e</b>) PC340, and (<b>f</b>) P25 films before and after QGDs surface modification.</p>
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<p>(<b>a</b>,<b>b</b>,<b>d</b>,<b>e</b>) TEM images of the QGD-PC261 film at different magnifications. (<b>c</b>,<b>f</b>) show the fast Fourier-transform (FFT) patterns of the areas indicated by circles in the high-resolution TEM images of (<b>b</b>,<b>e</b>), respectively.</p>
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<p>Ti 2p X-ray photoelectron XP spectra for the (<b>a</b>) PC261 and (<b>b</b>) GQD-PC261 films. C 1s XP spectra for the (<b>c</b>) PC261 and (<b>d</b>,<b>e</b>) GQD-PC261 films after surface modification for 24 h (48 h) impregnation. Solid lines show the total fit and the individual peak deconvolution. The <span class="html-italic">sp<sup>3</sup></span> component in (<b>c</b>,<b>d</b>) is attributed to adventitious carbon, while in (<b>e</b>) the <span class="html-italic">sp<sup>2</sup></span> component indicates GQDs presence.</p>
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<p>Raman spectra of the (<b>a</b>) PC211 and (<b>b</b>) PC261 films before and after GQDs’ surface modification at 514 nm.</p>
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<p>Salicylic acid (SA) (<b>a</b>) absorbance spectra, (<b>b</b>,<b>c</b>) photodegradation kinetics, (<b>d</b>) and reaction rates for the pristine and GQDs surface-modified PC and P25 TiO<sub>2</sub> films under UV–VIS light irradiation. Solid lines in (<b>c</b>) correspond to the best fit curves of the ln(<span class="html-italic">C</span>/<span class="html-italic">C</span><sub>0</sub>) vs. <span class="html-italic">t</span> plots.</p>
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<p>Salicylic acid (SA) (<b>a</b>) absorbance spectra, (<b>b</b>,<b>c</b>) photodegradation kinetics, and (<b>d</b>) reaction rates for the pristine and GQDs surface-modified PC and P25 TiO<sub>2</sub> films under visible light irradiation. Solid lines in (<b>c</b>) correspond to the best fit curves of the ln(<span class="html-italic">C</span>/<span class="html-italic">C</span><sub>0</sub>) vs. <span class="html-italic">t</span> plots.</p>
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<p>SA photodegradation kinetics by GQD-PC211 films under UV–VIS light for pH values of 3, 7, and 10 and in the presence of 0.01 M MeOH at pH = 3. (<b>a</b>) ln(<span class="html-italic">C</span>/<span class="html-italic">C</span><sub>0</sub>) vs. <span class="html-italic">t</span>; (<b>b</b>) ln(<span class="html-italic">C</span>/<span class="html-italic">C</span><sub>0</sub>) vs. <span class="html-italic">t</span> plots. The inset in (<b>b</b>) shows the corresponding reaction rates.</p>
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<p>(<b>a</b>) SA photodegradation kinetics for three successive tests using the same GQD-PC211 film under UV–VIS light; SEM images of GQD-PC261 (<b>b</b>) before and (<b>c</b>) after SA photodegradation.</p>
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<p>(<b>a</b>) Transient photocurrent density for pristine and surface-modified GQD-PC films under UV–VIS illumination; (<b>b</b>) EIS Nyquist plots for the PC211 and GQD-PC211 films under dark and UV–VIS illumination; (<b>c</b>) capacitance vs. applied potential for pristine and GQDs-modified PC and P25 films at 1000 Hz; (<b>d</b>) PL spectra for P25 and PC211 before and after GQDs surface modification. The inset in (<b>a</b>) shows the variation of photocurrent density (J) for GQD-PC211 films under continuous UV–VIS irradiation for 1 h at 1.23 V Ag/AgCl.</p>
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17 pages, 8008 KiB  
Article
Photoinduced Enhancement of Photoluminescence of Colloidal II-VI Nanocrystals in Polymer Matrices
by Volodymyr Dzhagan, Oleksandr Stroyuk, Oleksandra Raievska, Oksana Isaieva, Olga Kapush, Oleksandr Selyshchev, Volodymyr Yukhymchuk, Mykhailo Valakh and Dietrich R. T. Zahn
Nanomaterials 2020, 10(12), 2565; https://doi.org/10.3390/nano10122565 - 21 Dec 2020
Cited by 7 | Viewed by 3059
Abstract
The environment strongly affects both the fundamental physical properties of semiconductor nanocrystals (NCs) and their functionality. Embedding NCs in polymer matrices is an efficient way to create a desirable NC environment needed for tailoring the NC properties and protecting NCs from adverse environmental [...] Read more.
The environment strongly affects both the fundamental physical properties of semiconductor nanocrystals (NCs) and their functionality. Embedding NCs in polymer matrices is an efficient way to create a desirable NC environment needed for tailoring the NC properties and protecting NCs from adverse environmental factors. Luminescent NCs in optically transparent polymers have been investigated due to their perspective applications in photonics and bio-imaging. Here, we report on the manifestations of photo-induced enhancement of photoluminescence (PL) of aqueous colloidal NCs embedded in water-soluble polymers. Based on the comparison of results obtained on bare and core/shell NCs, NCs of different compounds (CdSe, CdTe, ZnO) as well as different embedding polymers, we conclude on the most probable mechanism of the photoenhancement for these sorts of systems. Contrary to photoenhancement observed earlier as a result of surface photocorrosion, we do not observe any change in peak position and width of the excitonic PL. Therefore, we suggest that the saturation of trap states by accumulated photo-excited charges plays a key role in the observed enhancement of the radiative recombination. This suggestion is supported by the unique temperature dependence of the trap PL band as well as by power-dependent PL measurement. Full article
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<p>Representative optical absorption (dashed lines) and photoluminescence (PL) (solid lines, λ<sub>exc</sub> = 325 nm) of a series of about 3nm CdSe NCs and 4 nm core/shell NCs in gelatin matrix.</p>
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<p>Evolution (from black to blue) of the room-temperature PL spectra (λ<sub>exc</sub> = 325 nm, 0.1 W/cm<sup>2</sup>) of CdSe NCs in a gelatin matrix at different time-scales, with the periods between the spectra equal to 8 s (<b>a</b>) and 120 s (<b>b</b>). EPL and DPL denotes, respectively, the excitonic emission band and the trap/defect-related band. A representative deconvolution of the latter into two components, DPL1 and DPL2, is shown for the bottom spectrum in (<b>b</b>).</p>
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<p>A schematic representing the mechanism proposed in this work to interpret the photoinduced changes (photoenhancement) in the PL spectra of NCs in a polymer matrix. The dotted lines denote non-radiative transitions of the photoexcited carrier to the trap states (trapping). Charge carriers that fill the states and block PL emission from them are depictured in grey. The charge carriers in three other colors denote those available for different recombination mechanisms (indicated by an arrow of the same color): excitonic or near-bandgap PL (EPL, green); defect related PL bands DPL1 (yellow) and DPL2 (red). The evolution of the energy level filling upon NC photoexcitation is as follows: (<b>a</b>) initially both radiative and non-radiative traps are empty; (<b>b</b>) filling of the non-radiative traps and concomitant increase of an overall PL intensity; (<b>c</b>) partial filling of the radiative trap levels underlying DPL2 band leads to blue shift of the whole DPL band; (<b>d</b>) complete filling of the DPL2 trap levels and disappearance of DPL2 contribution from the spectrum.</p>
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<p>Evolution (from black to blue) of the room-temperature PL spectra (λ<sub>exc</sub> = 325 nm, 0.1 W/cm<sup>2</sup>) of CdSe/ZnS NCs in gelatin matrix, with the periods between the spectra equal to 8 s (<b>a</b>) and 120 s (<b>b</b>).</p>
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<p>(<b>a</b>) Time evolution of the room-temperature PL intensity (λ<sub>exc</sub> = 325 nm) of CdSe, CdSe/CdS, and CdSe/ZnS NCs in gelatin matrix. The integrated PL intensity was derived from the time-resolved series of spectra like those in the <a href="#nanomaterials-10-02565-f002" class="html-fig">Figure 2</a> and <a href="#nanomaterials-10-02565-f004" class="html-fig">Figure 4</a>. The inset shows the same dependences but in a full intensity range of the EPL of CdSe/ZnS (<b>b</b>) Evolution (from black to green) of the room-temperature PL spectra (λ<sub>exc</sub> = 325 nm) of CdSe NCs in PVA matrix.</p>
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<p>(<b>a</b>) Time evolution (from black to blue) of the PL intensity of CdSe (<b>a</b>) and CdSe/ZnS (<b>b</b>) NCs in gelatin matrix at λ<sub>exc</sub> = 457.9 nm (0.1 W/cm<sup>2</sup>).</p>
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<p>Temperature dependence of the PL spectra of CdSe (<b>a</b>) and CdSe/ZnS (<b>b</b>) NCs in gelatin matrix (λ<sub>exc</sub> = 441.7 nm, 0.1 W/cm<sup>2</sup>).</p>
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<p>Temperature dependence of the PL spectra of CdSe (<b>a</b>) and CdSe/ZnS (<b>b</b>) NCs in gelatin matrix (λ<sub>exc</sub> = 514.5 nm, 0.1 W/cm<sup>2</sup>). Inset in (<b>b</b>) shows normalized curves.</p>
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<p>Temperature dependence of the peak position (<b>a</b>) and FWHM (<b>b</b>) of EPL and DPL bands of CdSe, CdSe, and CdSe/ZnS NCs stabilized with gelatin (λ<sub>exc</sub> = 441.7 nm, 0.1 W/cm<sup>2</sup>). The schematic in (<b>c</b>) illustrates the assumed mechanism behind the observed red shift of the trap-related PL with temperature decrease.</p>
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<p>(<b>a</b>) Evolution of the representative room-temperature PL spectra (λ<sub>exc</sub> = 325 nm, 0.1 W/cm<sup>2</sup>) of CdTe/CdS NCs embedded in gelatin. (<b>b</b>) Time-dependent behavior of PL intensity (λ<sub>exc</sub> = 515 nm, power density indicated in the legend) CdTe/CdS NCs embedded in gelatin and PEG at different volumetric ratios of NC:polymer.</p>
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<p>Evolution of the room-temperature PL spectra (λ<sub>exc</sub> = 325 nm, 0.1 W/cm<sup>2</sup>) of ZnO NCs in a matrix of PVA (<b>a</b>), gelatin (<b>b</b>), and PEDOT:PSS (<b>c</b>). The temperature dependence of PL of ZnO NCs in PEDOT:PSS is shown in (<b>d</b>). The waviness of the PL curve in (<b>b</b>) is due to interference in the polymer film.</p>
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<p>Evolution of the representative room-temperature PL spectra of ZnO NCs in solution as a function of the laser excitation power (λ<sub>exc</sub> = 325 nm).</p>
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<p>Schematic representation of the NC/polymer interface, including an optional ligand shell formed in case of ex situ synthesized NCs (see text for details and discussion).</p>
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<p>Illustration of the reversibility of the PL photoenhancement for both CdSe (<b>a</b>) and CdSe/ZnS NCs (<b>b</b>) at λ<sub>exc</sub> = 325 nm.</p>
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12 pages, 875 KiB  
Article
Strategies to Improve the Properties of Amaranth Protein Isolate-Based Thin Films for Food Packaging Applications: Nano-Layering through Spin-Coating and Incorporation of Cellulose Nanocrystals
by Amparo López-Rubio, Adriana Blanco-Padilla, Kristiina Oksman and Sandra Mendoza
Nanomaterials 2020, 10(12), 2564; https://doi.org/10.3390/nano10122564 - 21 Dec 2020
Cited by 18 | Viewed by 3431
Abstract
In this work, two different strategies for the development of amaranth protein isolate (API)-based films were evaluated. In the first strategy, ultrathin films were produced through spin-coating nanolayering, and the effects of protein concentration in the spin coating solution, rotational speed, and number [...] Read more.
In this work, two different strategies for the development of amaranth protein isolate (API)-based films were evaluated. In the first strategy, ultrathin films were produced through spin-coating nanolayering, and the effects of protein concentration in the spin coating solution, rotational speed, and number of layers deposited on the properties of the films were evaluated. In the second strategy, cellulose nanocrystals (CNCs) were incorporated through a casting methodology. The morphology, optical properties, and moisture affinity of the films (water contact angle, solubility, water content) were characterized. Both strategies resulted in homogeneous films with good optical properties, decreased hydrophilic character (as deduced from the contact angle measurements and solubility), and improved mechanical properties when compared with the neat API-films. However, both the processing method and film thickness influenced the final properties of the films, being the ones processed through spin coating more transparent, less hydrophilic, and less water-soluble. Incorporation of CNCs above 10% increased hydrophobicity, decreasing the water solubility of the API films and significantly enhancing material toughness. Full article
(This article belongs to the Special Issue Nanocomposites for Food Packaging)
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<p>Visual appearance of cast vs. spin-coated amaranth-based films. Cast films: (<b>A</b>) API, (<b>B</b>) API + CNC 5%, (<b>C</b>) API + CNC 10%, (<b>D</b>) API + CNC 20% films. Spin-coated films obtained from solutions containing 5% (<b>E</b>–<b>G</b>), 10% (<b>H</b>–<b>J</b>) or 15% API (<b>K</b>–<b>M</b>) and 25 (<b>E</b>,<b>H</b>,<b>K</b>), 50 (<b>H</b>–<b>J</b>) or 100 layers (<b>K</b>–<b>M</b>).</p>
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<p>UV-Visible light transmission of the (<b>A</b>) cast films and (<b>B</b>) spin-coated films.</p>
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11 pages, 599 KiB  
Article
Plasmon-Enhanced Fluorescence of EGFP on Short-Range Ordered Ag Nanohole Arrays
by Vladimir E. Bochenkov, Ekaterina M. Lobanova, Aleksander M. Shakhov, Artyom A. Astafiev, Alexey M. Bogdanov, Vadim A. Timoshenko and Anastasia V. Bochenkova
Nanomaterials 2020, 10(12), 2563; https://doi.org/10.3390/nano10122563 - 20 Dec 2020
Cited by 2 | Viewed by 3602
Abstract
Fluorescence of organic molecules can be enhanced by plasmonic nanostructures through coupling to their locally amplified electromagnetic field, resulting in higher brightness and better photostability of fluorophores, which is particularly important for bioimaging applications involving fluorescent proteins as genetically encoded biomarkers. Here, we [...] Read more.
Fluorescence of organic molecules can be enhanced by plasmonic nanostructures through coupling to their locally amplified electromagnetic field, resulting in higher brightness and better photostability of fluorophores, which is particularly important for bioimaging applications involving fluorescent proteins as genetically encoded biomarkers. Here, we show that a hybrid bionanosystem comprised of a monolayer of Enhanced Green Fluorescent Protein (EGFP) covalently linked to optically thin Ag films with short-range ordered nanohole arrays can exhibit up to 6-fold increased brightness. The largest enhancement factor is observed for nanohole arrays with a propagating surface plasmon mode, tuned to overlap with both excitation and emission of EGFP. The fluorescence lifetime measurements in combination with FDTD simulations provide in-depth insight into the origin of the fluorescence enhancement, showing that the effect is due to the local amplification of the optical field near the edges of the nanoholes. Our results pave the way to improving the photophysical properties of hybrid bionanosystems based on fluorescent proteins at the interface with easily fabricated and tunable plasmonic nanostructures. Full article
(This article belongs to the Special Issue Photonic Nanomaterials)
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Figure 1
<p>Simplified schematic of the experiment showing the short-range ordered (SRO) nanoholes in the optically thin silver film with immobilized Enhanced Green Fluorescent Protein (EGFP) and the illumination configuration.</p>
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<p>EGFP fluorescence enhancement by the Ag nanohole arrays. (<b>A</b>) Normalized extinction spectra of various Ag nanohole arrays (NHAs) (colored lines) and normalized absorption (blue) and emission (green) of EGFP (filled area). (<b>B</b>) Relative emission intensity of EGFP immobilized on glass (black) and on AgNHAs (colored lines). The legend indicates the SPR peak positions. (<b>C</b>) Fluorescence enhancement factors. The same color code is used in all panels.</p>
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<p>Fluorescence decay kinetics of EGFP immobilized on glass (red dots) and AgNHA (green dots) with the corresponding fits (red and green lines, respectively). Shown is also the instrument response function (blue line).</p>
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<p>Simulation of the EGFP fluorescence enhancement near periodic 100 nm AgNHA. (<b>A</b>) Top and section views of the simulated periodic box; the blue and red dots indicate the positions of a dipole source during the scan (the same color code is used in panels <b>B</b>,<b>C</b>) Extinction (1-T) spectrum of Ag NHA (blue line). The excitation and oscillating dipole emission wavelengths are shown by the blue and green dashed lines, respectively. (<b>C</b>) Excited state lifetime. (<b>D</b>) Fluorescence enhancement factor.</p>
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14 pages, 16363 KiB  
Article
Impact of Inductively Coupled Plasma Etching Conditions on the Formation of Semi-Polar (\({11\overline{2}2}\)) and Non-Polar (\({11\overline{2}0}\)) GaN Nanorods
by Pierre-Marie Coulon, Peng Feng, Tao Wang and Philip A. Shields
Nanomaterials 2020, 10(12), 2562; https://doi.org/10.3390/nano10122562 - 20 Dec 2020
Cited by 3 | Viewed by 3860
Abstract
The formation of gallium nitride (GaN) semi-polar and non-polar nanostructures is of importance for improving light extraction/absorption of optoelectronic devices, creating optical resonant cavities or reducing the defect density. However, very limited studies of nanotexturing via dry etching have been performed, in comparison [...] Read more.
The formation of gallium nitride (GaN) semi-polar and non-polar nanostructures is of importance for improving light extraction/absorption of optoelectronic devices, creating optical resonant cavities or reducing the defect density. However, very limited studies of nanotexturing via dry etching have been performed, in comparison to wet etching. In this paper, we investigate the formation and morphology of semi-polar (112¯2) and non-polar (112¯0) GaN nanorods using inductively coupled plasma (ICP) etching. The impact of gas chemistry, pressure, temperature, radio-frequency (RF) and ICP power and time are explored. A dominant chemical component is found to have a significant impact on the morphology, being impacted by the polarity of the planes. In contrast, increasing the physical component enables the impact of crystal orientation to be minimized to achieve a circular nanorod profile with inclined sidewalls. These conditions were obtained for a small percentage of chlorine (Cl2) within the Cl2 + argon (Ar) plasma combined with a low pressure. Damage to the crystal was reduced by lowering the direct current (DC) bias through a reduction of the RF power and an increase of the ICP power. Full article
(This article belongs to the Special Issue Nano-Fabrication Technology and Applications)
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Figure 1
<p>(<b>a</b>) Sketch of the process flow for fabrication of gallium nitride (GaN) nanorods. Plan view and cross-sectional (inset) scanning electron microscopy (SEM) image of nickel mask on (<b>b</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>c</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 1 with different ratios of Cl<sub>2</sub>/Ar flow rates for (<b>a</b>–<b>c</b>) <span class="html-italic">c</span>-plane (<b>d</b>–<b>f</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>g</b>–<b>i</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>Etch rate of the <span class="html-italic">c</span>-plane, (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) the non-polar GaN layers as a function of the Cl<sub>2</sub>/Ar ratio.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 2 under different chamber pressures for (<b>a</b>–<b>d</b>) <span class="html-italic">c</span>-plane (<b>e</b>–<b>h</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>i</b>–<b>l</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>(<b>a</b>) Etch rate, (<b>b</b>) base diameter and (<b>c</b>) sidewall angle of <span class="html-italic">c</span>-plane, (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers as a function of the pressure. The pedestal diameter and sidewall angle are schematically described in (<b>b</b>,<b>c</b>), respectively.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 3 under different chamber pressures for (<b>a</b>,<b>b</b>) <span class="html-italic">c</span>-plane (<b>c</b>,<b>d</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>e</b>,<b>f</b>) (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 4 under different chamber temperatures for (<b>a</b>–<b>d</b>) <span class="html-italic">c</span>-plane (<b>e</b>–<b>h</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>i</b>–<b>l</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>(<b>a</b>) Etch rate, (<b>b</b>) base diameter and (<b>c</b>) sidewall angle of <span class="html-italic">c</span>-plane, (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers as a function of temperature.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 5 with different radio-frequency (RF) powers for (<b>a</b>–<b>c</b>) <span class="html-italic">c</span>-plane (<b>d</b>–<b>f</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>g</b>–<b>i</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>(<b>a</b>) Etch rate, (<b>b</b>) base diameter and (<b>c</b>) sidewall angle of the <span class="html-italic">c</span>-plane, (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers as a function of RF power.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 6 with different inductively coupled plasma (ICP) power for (<b>a</b>–<b>c</b>) <span class="html-italic">c</span>-plane (<b>d</b>–<b>f</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>g</b>–<b>i</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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<p>(<b>a</b>) Etch rate, (<b>b</b>) base diameter and (<b>c</b>) sidewall angle of <span class="html-italic">c</span>-plane. (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<math display="inline"><semantics> <mrow> <mn>11</mn> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers as a function of ICP power.</p>
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<p>Plan view and cross-sectional (inset) SEM image of GaN nanorod etch series 7 and 8 with different times for two etching conditions, for (<b>a</b>–<b>d</b>) <span class="html-italic">c</span>-plane (<b>e</b>–<b>h</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>2</mn> </mrow> </semantics></math>) semi-polar and (<b>i</b>–<b>l</b>) (11<math display="inline"><semantics> <mrow> <mover accent="true"> <mn>2</mn> <mo>¯</mo> </mover> <mn>0</mn> </mrow> </semantics></math>) non-polar GaN layers. Scale bar is 1 µm.</p>
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25 pages, 5147 KiB  
Article
Biodegradable PLA/PBSA Multinanolayer Nanocomposites: Effect of Nanoclays Incorporation in Multinanolayered Structure on Mechanical and Water Barrier Properties
by Tiphaine Messin, Nadège Follain, Quentin Lozay, Alain Guinault, Nicolas Delpouve, Jérémie Soulestin, Cyrille Sollogoub and Stéphane Marais
Nanomaterials 2020, 10(12), 2561; https://doi.org/10.3390/nano10122561 - 20 Dec 2020
Cited by 8 | Viewed by 3493
Abstract
Biodegradable PLA/PBSA multinanolayer nanocomposites were obtained from semi-crystalline poly(butylene succinate-co-butylene adipate) (PBSA) nanolayers filled with nanoclays and confined against amorphous poly(lactic acid) (PLA) nanolayers in a continuous manner by applying an innovative coextrusion technology. The cloisite 30B (C30B) filler incorporation in [...] Read more.
Biodegradable PLA/PBSA multinanolayer nanocomposites were obtained from semi-crystalline poly(butylene succinate-co-butylene adipate) (PBSA) nanolayers filled with nanoclays and confined against amorphous poly(lactic acid) (PLA) nanolayers in a continuous manner by applying an innovative coextrusion technology. The cloisite 30B (C30B) filler incorporation in nanolayers was considered to be an improvement of barrier properties of the multilayer films additional to the confinement effect resulting to forced assembly during the multilayer coextrusion process. 2049-layer films of ~300 µm thick were processed containing loaded PBSA nanolayers of ~200 nm, which presented certain homogeneity and were mostly continuous for the 80/20 wt% PLA/PBSA composition. The nanocomposite PBSA films (monolayer) were also processed for comparison. The presence of exfoliated and intercalated clay structure and some aggregates were observed within the PBSA nanolayers depending on the C30B content. A greater reduction of macromolecular chain segment mobility was measured due to combined effects of confinement effect and clays constraints. The absence of both polymer and clays interdiffusions was highlighted since the PLA glass transition was unchanged. Besides, a larger increase in local chain rigidification was evidenced through RAF values due to geometrical constraints initiated by close nanoclay contact without changing the crystallinity of PBSA. Tortuosity effects into the filled PBSA layers adding to confinement effects induced by PLA layers have caused a significant improvement of water barrier properties through a reduction of water permeability, water vapor solubility and water vapor diffusivity. The obtaining barrier properties were successfully correlated to microstructure, thermal properties and mobility of PBSA amorphous phase. Full article
(This article belongs to the Special Issue Functional Biodegradable Nanocomposites)
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<p>TEM observations for PBSA filled with (<b>a</b>) 2% and (<b>b</b>) 5 wt% of montmorillonite C30B.</p>
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<p>XRD spectra of neat PBSA film and filled PBSA films (<b>a</b>) in the 15–40° range and (<b>b</b>) in the 2–14° range.</p>
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<p>TGA curves obtained for the neat PBSA film and the filled PBSA films.</p>
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<p>Reduced water permeation curves for the neat PBSA and the filled PBSA films.</p>
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<p>Water permeation curves for the neat PBSA and the filled PBSA films fitted using a model combining two sorption modes, the Henry-law sorption and the aggregation (clustering) sorption, as represented in Equation (9).</p>
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<p>Water vapor diffusion coefficients <span class="html-italic">D</span><sub>1</sub> and <span class="html-italic">D</span><sub>2</sub> for the neat PBSA and the filled PBSA films.</p>
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<p>TEM observations of the unfilled PLA/PBSA and filled PLA/PBSA2 and PLA/PBSA5 multilayer films (PLA in white, PBSA in dark). (AFM image of unfilled PLA/PBSA multilayer films).</p>
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<p>XRD spectra for the PLA/PBSA, PLA/PBSA2 and PLA/PBSA5 multilayer films in the 5–40° range (<b>a</b>) and for C30B powder in 2–14° range (<b>b</b>).</p>
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<p>Reduced water permeation curves for the PLA/PBSA multilayer film and the filled PLA/PBSA multilayer films.</p>
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<p>Comparison of the experimental and predicted permeabilities of PBSA under monolayer and multilayer films. <span style="color:blue">▲</span> IF1: calculated from neat PBSA—effect of loading <span style="color:red">♦</span> IF2: calculated from PBSA (neat of filled)—effect of multilayer <span style="color:#538135">■</span> IF3: calculated from neat PBSA—effect of loading and multilayer.</p>
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<p>Water vapor sorption isotherms for the PLA/PBSA, PLA/PBSA2 and PLA/PBSA5 multilayer films modelled by two consecutive sorption modes, the Henry-law sorption and the aggregation (clustering) sorption, as represented in Equation (9).</p>
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<p>Water vapor diffusion coefficients <span class="html-italic">D</span><sub>1</sub> and <span class="html-italic">D</span><sub>2</sub> for the PLA/PBSA, PLA/PBSA2 and PLA/PBSA5 multilayer films.</p>
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20 pages, 4763 KiB  
Article
Thiolation of Chitosan Loaded over Super-Magnetic Halloysite Nanotubes for Enhanced Laccase Immobilization
by Avinash A. Kadam, Bharat Sharma, Surendra K. Shinde, Gajanan S. Ghodake, Ganesh D. Saratale, Rijuta G. Saratale, Do-Yeong Kim and Jung-Suk Sung
Nanomaterials 2020, 10(12), 2560; https://doi.org/10.3390/nano10122560 - 20 Dec 2020
Cited by 18 | Viewed by 3780
Abstract
This study focuses on the development of a nanosupport based on halloysite nanotubes (HNTs), Fe3O4 nanoparticles (NPs), and thiolated chitosan (CTs) for laccase immobilization. First, HNTs were modified with Fe3O4 NPs (HNTs-Fe3O4) by [...] Read more.
This study focuses on the development of a nanosupport based on halloysite nanotubes (HNTs), Fe3O4 nanoparticles (NPs), and thiolated chitosan (CTs) for laccase immobilization. First, HNTs were modified with Fe3O4 NPs (HNTs-Fe3O4) by the coprecipitation method. Then, the HNTs-Fe3O4 surface was tuned with the CTs (HNTs-Fe3O4-CTs) by a simple refluxing method. Finally, the HNTs- Fe3O4-CTs surface was thiolated (-SH) (denoted as; HNTs- Fe3O4-CTs-SH) by using the reactive NHS-ester reaction. The thiol-modified HNTs (HNTs- Fe3O4-CTs-SH) were characterized by FE-SEM, HR-TEM, XPS, XRD, FT-IR, and VSM analyses. The HNTs-Fe3O4-CTs-SH was applied for the laccase immobilization. It gave excellent immobilization of laccase with 100% activity recovery and 144 mg/g laccase loading capacity. The immobilized laccase on HNTs-Fe3O4-CTs-SH (HNTs-Fe3O4-CTs-S-S-Laccase) exhibited enhanced biocatalytic performance with improved thermal, storage, and pH stabilities. HNTs-Fe3O4-CTs-S-S-Laccase gave outstanding repeated cycle capability, at the end of the 15th cycle, it kept 61% of the laccase activity. Furthermore, HNTs-Fe3O4-CTs-S-S-Laccase was applied for redox-mediated removal of textile dye DR80 and pharmaceutical compound ampicillin. The obtained result marked the potential of the HNTs-Fe3O4-CTs-S-S-Laccase for the removal of hazardous pollutants. This nanosupport is based on clay mineral HNTs, made from low-cost biopolymer CTs, super-magnetic in nature, and can be applied in laccase-based decontamination of environmental pollutants. This study also gave excellent material HNTs-Fe3O4-CTs-SH for other enzyme immobilization processes. Full article
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Figure 1
<p>The schematic presentation of the synthesis of(<b>A</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs, (<b>B</b>) reactive NHS ester, and (<b>C</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase, and (<b>D</b>) degradation of the environmental contaminants Direct Red 80 and ampicillin by the immobilized laccase.</p>
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<p>SEM analysis of (<b>A</b>) HNTs, and (<b>B</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH. HR-TEM analysis of the HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH (<b>C</b>) inset (i) SAED pattern of the HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH. The STEM HAADF image of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH (<b>D</b>), elemental mapping of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH (<b>E</b>), and corresponding elemental distribution of Si (<b>F</b>), O (<b>G</b>), Al (<b>H</b>), Fe (<b>I</b>), C (<b>J</b>), N (<b>K</b>) and S (<b>L</b>).</p>
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<p><b>(A</b>) HR-TEM EDS analysis of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH, (<b>B</b>) XRD analysis of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH, (<b>C</b>) FT-IR analysis of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs, HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH, and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase (<b>D</b>) VSM analysis of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase inset (<b>i</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase without magnet, and (<b>ii</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase with magnet, (<b>E</b>) XPS analysis of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase.</p>
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<p>The high-resolution XPS spectrum of the Fe 2p peaks of (<b>A</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs, and (<b>B</b>) HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase.</p>
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<p>(<b>A</b>) Unit activity of free laccase (0.1 mL from 1.5 mg/mL laccase solution in sodium acetate buffer (100 mM, pH 4)), laccase immobilized on HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs (0.1 mL solution containing 1 mg of laccase immobilized HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs in sodium acetate buffer (100 mM, pH 4)), and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase (0.1 mL solution containing 1 mg of HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase in sodium acetate buffer (100 mM, pH 4)). (<b>B</b>) Photographic image representing the color change after the oxidation of ABTS by free laccase and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase.</p>
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<p>(<b>A</b>) Effect of initial laccase concentration on the immobilization on the HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-SH, (<b>B</b>) temperature stability at 60 °C for 200 min by free laccase and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase, (<b>C</b>) storage stability for 30 days by free laccase and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase, (<b>D</b>) pH stabilities free laccase and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase, and (<b>E</b>) repeated cycle activities of the HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase.</p>
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<p>Structures of the environmental pollutants Direct Red 80 and ampicillin, and redox mediators, p-coumaric acid (CA), 1-1-hydroxy benzotriazole hydrate (HBT), syringaldehyde (SA), guaiacol (GUA), and 2,2′-Azino-bis(3-ethylbenzothiazoline-6-sulfonic acid) (ABTS).</p>
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<p>Removal of the DR80 by free laccase and HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase; without a mediator (WM), and with redox mediators of CA, HBT, SA, GUA, and ABTS.</p>
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<p>Effect of pH on removal of the DR80 by HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase in the presence of the redox mediator ABTS.</p>
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<p>Repeated cycle removal of the DR80 by HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase in the presence of the redox mediator ABTS.</p>
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<p>HPLC analysis of the ampicillin degradation by HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase (<b>A</b>) control ampicillin, (<b>B</b>) ampicillin + HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase (in absence of the redox mediator), (<b>C</b>) ampicillin + HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase + ABTS, (<b>D</b>) ampicillin + HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase + GUA, (<b>E</b>) ampicillin + HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase + SA, and (<b>F</b>) ampicillin + HNTs-Fe<sub>3</sub>O<sub>4</sub>-CTs-S-S-Laccase + HBT.</p>
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11 pages, 2245 KiB  
Article
Combined Toxicity of TiO2 Nanospherical Particles and TiO2 Nanotubes to Two Microalgae with Different Morphology
by Zhuang Wang, Shiguang Jin, Fan Zhang and Degao Wang
Nanomaterials 2020, 10(12), 2559; https://doi.org/10.3390/nano10122559 - 20 Dec 2020
Cited by 11 | Viewed by 3129
Abstract
The joint activity of multiple engineered nanoparticles (ENPs) has attracted much attention in recent years. Many previous studies have focused on the combined toxicity of different ENPs with nanostructures of the same dimension. However, the mixture toxicity of multiple ENPs with different dimensions [...] Read more.
The joint activity of multiple engineered nanoparticles (ENPs) has attracted much attention in recent years. Many previous studies have focused on the combined toxicity of different ENPs with nanostructures of the same dimension. However, the mixture toxicity of multiple ENPs with different dimensions is much less understood. Herein, we investigated the toxicity of the binary mixture of TiO2 nanospherical particles (NPs) and TiO2 nanotubes (NTs) to two freshwater algae with different morphology, namely, Scenedesmus obliquus and Chlorella pyrenoidosa. The physicochemical properties, dispersion stability, and the generation of reactive oxygen species (ROS) were determined in the single and binary systems. Classical approaches to assessing mixture toxicity were applied to evaluate and predict the toxicity of the binary mixtures. The results show that the combined toxicity of TiO2 NPs and NTs to S. obliquus was between the single toxicity of TiO2 NTs and NPs, while the combined toxicity to C. pyrenoidosa was higher than their single toxicity. Moreover, the toxicity of the binary mixtures to C. pyrenoidosa was higher than that to S. obliquus. A toxic unit assessment showed that the effects of TiO2 NPs and NTs were additive to the algae. The combined toxicity to S. obliquus and C. pyrenoidosa can be effectively predicted by the concentration addition model and the independent action model, respectively. The mechanism of the toxicity caused by the binary mixtures of TiO2 NPs and NTs may be associated with the dispersion stability of the nanoparticles in aquatic media and the ROS-induced oxidative stress effects. Our results may offer a new insight into evaluating and predicting the combined toxicological effects of ENPs with different dimensions and of probing the mechanisms involved in their joint toxicity. Full article
(This article belongs to the Special Issue Advances in Nanotoxicology)
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<p>TEM images of the TiO<sub>2</sub> NPs (<b>A</b>), TiO<sub>2</sub> NTs (<b>B</b>), and TiO<sub>2</sub> NPs + NTs (<b>C</b>) in the algae medium.</p>
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<p>Total potential energy (V<sub>T</sub>) curves for the TiO<sub>2</sub> particles in the single and binary systems at 0 h (<b>A</b>) and 96 h (<b>B</b>).</p>
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<p>Concentration-response curves for <span class="html-italic">Scenedesmus obliquus</span> (<b>A</b>) and <span class="html-italic">Chlorella pyrenoidosa</span> (<b>B</b>) exposed to TiO<sub>2</sub> NPs, TiO<sub>2</sub> NTs, and TiO<sub>2</sub> NPs + NTs.</p>
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<p>Observed toxic units (TUs) as converted from the toxicity data of <span class="html-italic">Scenedesmus obliquus</span> and <span class="html-italic">Chlorella pyrenoidosa</span> following exposure to mixtures of TiO<sub>2</sub> NPs and NTs, and subsequently plotted against expected TUs calculated on the basis of the median effect concentrations from the individual constituents present in the mixtures.</p>
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<p>Comparison between regression models of the observed (OBS) combined nanotoxicity and expected toxicity of the mixtures to <span class="html-italic">Scenedesmus obliquus</span> (<b>A</b>) and <span class="html-italic">Chlorella pyrenoidosa</span> (<b>B</b>) according to concentration addition (CA) and independent action (IA). The dashed-line and dotted-line represent the 95% confidence band and 95% prediction band of the experimental data points, respectively.</p>
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<p>Relative levels of reactive oxygen species (ROS) detected using 2′,7′-dichlorodihydrofluorescein diacetate (DCFH-DA) staining in <span class="html-italic">Scenedesmus obliquus</span> (<b>A</b>) and <span class="html-italic">Chlorella pyrenoidosa</span> (<b>B</b>) exposed to single TiO<sub>2</sub> NPs and TiO<sub>2</sub> NTs at each <span class="html-italic">EC</span><sub>10</sub> or <span class="html-italic">EC</span><sub>50</sub> value, as well as TiO<sub>2</sub> NPs + NTs at the <span class="html-italic">EC</span><sub>10</sub> or <span class="html-italic">EC</span><sub>50</sub> ratios. Statistical significance versus control group: * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, and *** <span class="html-italic">p</span> &lt; 0.001.</p>
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13 pages, 3496 KiB  
Article
Self-Assembled Few-Layered MoS2 on SnO2 Anode for Enhancing Lithium-Ion Storage
by Thang Phan Nguyen and Il Tae Kim
Nanomaterials 2020, 10(12), 2558; https://doi.org/10.3390/nano10122558 - 20 Dec 2020
Cited by 21 | Viewed by 3538
Abstract
SnO2 nanoparticles (NPs) have been used as reversible high-capacity anode materials in lithium-ion batteries, with reversible capacities reaching 740 mAh·g−1. However, large SnO2 NPs do not perform well in charge–discharge cycling. In this work, we report the incorporation of [...] Read more.
SnO2 nanoparticles (NPs) have been used as reversible high-capacity anode materials in lithium-ion batteries, with reversible capacities reaching 740 mAh·g−1. However, large SnO2 NPs do not perform well in charge–discharge cycling. In this work, we report the incorporation of MoS2 nanosheet (NS) layers with SnO2 NPs. SnO2 NPs of ~5 nm in diameter synthesized by a facile hydrothermal precipitation method. Meanwhile, MoS2 NSs of a few hundreds of nanometers to a few micrometers in lateral size were produced by top-down chemical exfoliation. The self-assembly of the MoS2 NS layer on the gas–liquid interface was first demonstrated to achieve up to 80% coverage of the SnO2 NP anode surface. The electrochemical properties of the pure SnO2 NPs and MoS2-covered SnO2 NP anodes were investigated. The results showed that the SnO2 electrode with a single-layer MoS2 NS film exhibited better electrochemical performance than the pure SnO2 anode in lithium storage applications. Full article
(This article belongs to the Special Issue Nanomaterials for Ion Battery Applications)
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<p>Illustration and photographs of self-assembled MoS<sub>2</sub> nanosheet (NS) on Cu substrate.</p>
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<p>Scanning electron microscope (SEM) images of (<b>a</b>,<b>b</b>) SnO<sub>2</sub> nanoparticle (NP) powder, (<b>c</b>,<b>d</b>) single-layer MoS<sub>2</sub> NS thin film on Cu electrode, and (<b>e</b>,<b>f</b>) M1SnO<sub>2</sub> anode.</p>
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<p>X-ray diffraction (XRD) patterns of (<b>a</b>) SnO<sub>2</sub> NPs and M3SnO<sub>2</sub> anode and (<b>b</b>) lithium-ion intercalated and exfoliated MoS<sub>2</sub> nanosheet.</p>
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<p>(<b>a</b>) Transmission electron microscope (TEM) image of SnO<sub>2</sub> NP; energy-dispersive X-ray spectroscopy (EDS) mapping of the elements (<b>b</b>) O and (<b>c</b>) Sn; (<b>d</b>) high-resolution TEM (HRTEM) image of SnO<sub>2</sub> NP with inset selected-area electron diffraction (SAED) pattern; (<b>e</b>) exfoliated MoS<sub>2</sub> NS with inset SAED pattern.</p>
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<p>Cyclic voltammetry (CV) profiles of (<b>a</b>) SnO<sub>2</sub> NS and (<b>b</b>–<b>d</b>) M1/M2/M3SnO<sub>2</sub> anodes over three cycles.</p>
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<p>Galvanostatic charge–discharge profiles of (<b>a</b>) SnO<sub>2</sub> NS and (<b>b</b>–<b>d</b>) M1/M2/M3SnO<sub>2</sub> anodes for the initial three cycles.</p>
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<p>Cyclic performances and Nyquist plots of (<b>a</b>) SnO<sub>2</sub> NPs and (<b>b</b>–<b>d</b>) M1/M2/M3SnO<sub>2</sub> anodes.</p>
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<p>Rate cycling performance of (<b>a</b>) bare SnO<sub>2</sub> electrode and (<b>b</b>) M1SnO<sub>2</sub> electrode at different current rates.</p>
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<p>SEM images of (<b>a</b>,<b>d</b>) SnO<sub>2</sub> electrode, (<b>b</b>,<b>e</b>) M1SnO<sub>2</sub> electrode and (<b>c</b>,<b>f</b>) M3SnO<sub>2</sub> electrode after 10 cycles at different magnifications.</p>
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10 pages, 3038 KiB  
Article
Plasmonic Gold Nanohole Arrays for Surface-Enhanced Sum Frequency Generation Detection
by Wei Guo, Bowen Liu, Yuhan He, Enming You, Yongyan Zhang, Shengchao Huang, Jingjing Wang and Zhaohui Wang
Nanomaterials 2020, 10(12), 2557; https://doi.org/10.3390/nano10122557 - 19 Dec 2020
Cited by 8 | Viewed by 3904
Abstract
Nobel metal nanohole arrays have been used extensively in chemical and biological systems because of their fascinating optical properties. Gold nanohole arrays (Au NHAs) were prepared as surface plasmon polariton (SPP) generators for the surface-enhanced sum-frequency generation (SFG) detection of 4-Mercaptobenzonitrile (4-MBN). The [...] Read more.
Nobel metal nanohole arrays have been used extensively in chemical and biological systems because of their fascinating optical properties. Gold nanohole arrays (Au NHAs) were prepared as surface plasmon polariton (SPP) generators for the surface-enhanced sum-frequency generation (SFG) detection of 4-Mercaptobenzonitrile (4-MBN). The angle-resolved reflectance spectra revealed that the Au NHAs have three angle-dependent SPP modes and two non-dispersive localized surface plasmon resonance (LSPR) modes under different structural orientation angles (sample surface orientation). An enhancement factor of ~30 was achieved when the SPP and LSPR modes of the Au NHAs were tuned to match the incident visible (VIS) and output SFG, respectively. This multi-mode matching strategy provided flexible controls and selective spectral windows for surface-enhanced measurements, and was especially useful in nonlinear spectroscopy where more than one light beam was involved. The structural orientation- and power-dependent performance demonstrated the potential of plasmonic NHAs in SFG and other nonlinear sensing applications, and provided a promising surface molecular analysis development platform. Full article
(This article belongs to the Special Issue Plasmonic Nanostructures and Their Applications)
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<p>Schematic illustration of the preparation processes of the gold nanohole arrays (Au NHAs).</p>
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<p>(<b>a</b>) SEM and (<b>b</b>) AFM images of the Au NHAs. (<b>c</b>) Cross-sections profile along the blue line in the AFM image.</p>
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<p>Angle-resolved reflection spectrum of the Au NHAs at different structural orientation angles (<b>a</b>) <span class="html-italic">ϕ</span> = 0° and (<b>b</b>) <span class="html-italic">ϕ</span> = 90°. Insets are the optical measurement configuration.</p>
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<p>SFG spectra of 4-MBN on Au NHAs (black) at <span class="html-italic">ϕ</span> = 90° and flat gold film (red) at ~57° incident angle (with 1 mW VIS, 5 mW IR, and 30 s acquisition time).</p>
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<p>(<b>a</b>) SFG spectra of 4-Mercaptobenzonitrile (4-MBN) on Au NHAs with different structural orientation angles (with 1 mW VIS, 5 mW IR, and 60 s acquisition time). Insets are the SFG optical configurations. (<b>b</b>) Structural orientation dependent reflectance spectra of Au NHAs at a 57.4° incident angle.</p>
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<p>VIS power-dependent (<b>a</b>) SFG intensity of 4-MBN and (<b>b</b>) SFG enhancement factor of the Au NHAs at <span class="html-italic">τ</span> = 1 ps (with 5 mW IR and 60 s acquisition time).</p>
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58 pages, 10060 KiB  
Review
Multimodal/Multifunctional Nanomaterials in (Bio)electrochemistry: Now and in the Coming Decade
by Paloma Yáñez-Sedeño, Araceli González-Cortés, Susana Campuzano and José Manuel Pingarrón
Nanomaterials 2020, 10(12), 2556; https://doi.org/10.3390/nano10122556 - 19 Dec 2020
Cited by 14 | Viewed by 4154
Abstract
Multifunctional nanomaterials, defined as those able to achieve a combined effect or more than one function through their multiple functionalization or combination with other materials, are gaining increasing attention in the last years in many relevant fields, including cargo targeted delivery, tissue engineering, [...] Read more.
Multifunctional nanomaterials, defined as those able to achieve a combined effect or more than one function through their multiple functionalization or combination with other materials, are gaining increasing attention in the last years in many relevant fields, including cargo targeted delivery, tissue engineering, in vitro and/or in vivo diseases imaging and therapy, as well as in the development of electrochemical (bio)sensors and (bio)sensing strategies with improved performance. This review article aims to provide an updated overview of the important advances and future opportunities exhibited by electrochemical biosensing in connection to multifunctional nanomaterials. Accordingly, representative aspects of recent approaches involving metal, carbon, and silica-based multifunctional nanomaterials are selected and critically discussed, as they are the most widely used multifunctional nanomaterials imparting unique capabilities in (bio)electroanalysis. A brief overview of the main remaining challenges and future perspectives in the field is also provided. Full article
(This article belongs to the Special Issue Electrochemistry of Nanomaterials and/or Nanostructures)
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<p>Scheme of aptasensing assays for the detection of kanamycin (<b>A</b>) and <span class="html-italic">P. aeruginosa</span> (<b>B</b>) using inhibition of AuNPs peroxidase activity. Reproduced from [<a href="#B44-nanomaterials-10-02556" class="html-bibr">44</a>] (<b>A</b>) and [<a href="#B26-nanomaterials-10-02556" class="html-bibr">26</a>] (<b>B</b>), with permission.</p>
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<p>Schematic display of (<b>A</b>) the signal-amplified electrochemical biosensor for the detection of rHuEPO glycoprotein by using MBA-biotin-AuNPs as labels; (<b>B</b>) the label-free detection of miRNAs based on the triple signal amplification of APBA-biotin-AuNPs, SA-ALP, and the p-APredox-cycling reaction; and (<b>C</b>) the thyroxine biosensor in conditions of (up) absence and (down) presence of the analyte. Reproduced from [<a href="#B34-nanomaterials-10-02556" class="html-bibr">34</a>] (<b>A</b>), [<a href="#B35-nanomaterials-10-02556" class="html-bibr">35</a>] (<b>B</b>), and [<a href="#B38-nanomaterials-10-02556" class="html-bibr">38</a>] (<b>C</b>) with permission.</p>
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<p>Scheme of the strategy for the electrochemical determination of miRNA-21 using a nanocomposite of sodium alginate-polypyrrole/Au nanoparticles (SA-PPy/AuNPs). Reproduced from [<a href="#B36-nanomaterials-10-02556" class="html-bibr">36</a>] with permission.</p>
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<p>Schemes of (<b>A</b>) the preparation procedure of PtNi@Cu-TCPP(Fe)-Ab<sub>2</sub> bioconjugates and (<b>B</b>) the construction process of the electrochemical immunosensor for calprotectin (CALP). Reproduced from [<a href="#B12-nanomaterials-10-02556" class="html-bibr">12</a>] with permission.</p>
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<p>(<b>A</b>) Schematic display of the method for the detection of DNA hybridization using Ag-DNCs as label; (<b>B</b>) Fabrication and amperometric transduction involved in the development of an HRP-DAb-tau-CAb-3D-Au-PAMAM-<span class="html-italic">p</span>-ABA-SPCE immunosensor for the determination of tau protein. Reproduced from [<a href="#B32-nanomaterials-10-02556" class="html-bibr">32</a>] (<b>A</b>) and [<a href="#B21-nanomaterials-10-02556" class="html-bibr">21</a>] (<b>B</b>) with permission.</p>
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<p>Schematic illustration of a QD-based electrochemical biosensor for the stripping voltammetric detection of telomerase activity. Reproduced and adapted from [<a href="#B52-nanomaterials-10-02556" class="html-bibr">52</a>] with permission.</p>
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<p>Preparation of (<b>A</b>) the aptamer-functionalized AuNPs-Fe<sub>3</sub>O<sub>4</sub>-GS capture probes and (<b>B</b>) the aptamer/redox probes functionalized AuNPs. (<b>C</b>) Steps of capture, isolation, and multiplexed detection of target CTCs. Reproduced from [<a href="#B80-nanomaterials-10-02556" class="html-bibr">80</a>] with permission.</p>
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<p>Schematic illustration of the synthetic route of rGO/PdNFs nanohybrids (top) and applications in non-enzymatic glucose sensing, electrochemical catalysis of ethanol, and photothermal tumor therapy in vivo (bottom). Reproduced from [<a href="#B107-nanomaterials-10-02556" class="html-bibr">107</a>] with permission.</p>
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<p>Schematic illustration of the stepwise construction of an aptasensor for the determination of sulfadimethoxine (SDM) using fullerene-doped reduced graphene oxide nanohybrids. Reproduced from [<a href="#B118-nanomaterials-10-02556" class="html-bibr">118</a>] with permission.</p>
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<p>Preparation of carboxylated c-g-C<sub>3</sub>N<sub>4</sub> and Ab<sub>2</sub> bioconjugate (<b>up</b>) and sandwich-type immunosensor (<b>down</b>). Reproduced from [<a href="#B121-nanomaterials-10-02556" class="html-bibr">121</a>] with permission.</p>
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<p>Schematic display of the aptasensing strategy reported for the amperometric determination of CEA involving the use of aptamer and HRP bifunctionalized Au-MS JNPs, Av-Fe<sub>3</sub>O<sub>4</sub>@SiO<sub>2</sub> NPs and amperometric detection at SPCEs. Reprinted and adapted from [<a href="#B183-nanomaterials-10-02556" class="html-bibr">183</a>] with permission.</p>
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<p>Display of the electrochemical aptamer-based biosensing strategies using MSNs as gated nanomaterials. (<b>a</b>) MB-loaded Av/ImB-MSN as nanocarriers for signal amplification for the determination of CEA. (<b>b</b>) Glucose-loaded PDA-Apt-GAMMS for the determination of AFB1 using a PGM. Reprinted and adapted from [<a href="#B187-nanomaterials-10-02556" class="html-bibr">187</a>] (<b>a</b>) and [<a href="#B191-nanomaterials-10-02556" class="html-bibr">191</a>] (<b>b</b>) with permission.</p>
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<p>Impedimetric aptasensor for CEA using an AuNPs/AMSNs-GCE as transduction interface. Reprinted and adapted from [<a href="#B154-nanomaterials-10-02556" class="html-bibr">154</a>] with permission.</p>
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<p>(<b>a</b>) Schematic display of the GCE/MWCNTs-MCM41-Hb bioplatform. Cyclic voltammograms obtained in a N<sub>2</sub>-saturated 0.050 M phosphate buffer solution pH 7.00 in the absence (black) and presence (blue) of 1.5 × 10<sup>−2</sup> M NaNO<sub>2</sub> (<b>b</b>) and 0.100 M TCA (<b>c</b>) at GCE/MWCNTs-MCM41-Hb. Inset: corresponding CVs obtained at GCE/MWCNTs. Reprinted and adapted from [<a href="#B165-nanomaterials-10-02556" class="html-bibr">165</a>] with permission.</p>
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<p>Sandwich aptasensors for thrombin developed at a PAMAM–rGO-GCE using mSiO<sub>2</sub>@MWCNT decorated with Thi, platinum nanoparticles (PtNPs), and hemin/G-quadruplex bioelectrocatalytic complex as bionanolabels (<b>a</b>) or a HDGMs-modified GCE using Thi-GMNs as signaling tags (<b>b</b>). (<b>c</b>) Competitive immunosensor for STR developed at a TRSiNs (Thi)-GCE using GMSNs carrying STR-BSA and HRP. Reprinted and adapted from [<a href="#B178-nanomaterials-10-02556" class="html-bibr">178</a>] (<b>a</b>) [<a href="#B151-nanomaterials-10-02556" class="html-bibr">151</a>] (<b>b</b>) and [<a href="#B192-nanomaterials-10-02556" class="html-bibr">192</a>] (<b>c</b>) with permission.</p>
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<p>Sandwich electrochemical immunosensors developed for: (<b>a</b>) the determination of CEA using Fe<sub>3</sub>O<sub>4</sub>@SiO<sub>2</sub>–Fc–DAb/HRP nanobioconjugates and (<b>b</b>) the simultaneous determination of Bcl-2 and Bax using mesoporous SiO<sub>2</sub> decorated with DAb and CdSeTe@CdS quantum dots (QDs) or Ag nanoclusters (NCs). Reprinted and adapted from [<a href="#B182-nanomaterials-10-02556" class="html-bibr">182</a>] (<b>a</b>) and [<a href="#B180-nanomaterials-10-02556" class="html-bibr">180</a>] (<b>b</b>) with permission.</p>
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<p>DNA biosensor for the determination of <span class="html-italic">BRCA-1</span> using DNA-modified SiO<sub>2</sub>@AgNPs as tracing tags. Reprinted and adapted from [<a href="#B193-nanomaterials-10-02556" class="html-bibr">193</a>] with permission.</p>
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<p>Use of DAb and HRP-loaded SiO<sub>2</sub>-SPAABs (<b>a</b>) and AuNPs-Si MSs decorated with Zn<sup>2+</sup> and DAb as labels (<b>b</b>) in the preparation of an electrochemical immunosensor and an aptasensor for the determination of HIgG and CRP, respectively. Reprinted and adapted from [<a href="#B194-nanomaterials-10-02556" class="html-bibr">194</a>] (<b>a</b>) and [<a href="#B195-nanomaterials-10-02556" class="html-bibr">195</a>] (<b>b</b>) with permission.</p>
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<p>Label-free electrochemical aptasensor for PSA detection developed at an MSF-AuE. Reprinted and adapted from [<a href="#B176-nanomaterials-10-02556" class="html-bibr">176</a>] with permission.</p>
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15 pages, 2043 KiB  
Article
Synergic Effect of Novel WS2 Carriers Holding Spherical Cobalt Ferrite @cubic Fe3O4 (WS2/s-CoFe2O4@c-Fe3O4) Nanocomposites in Magnetic Resonance Imaging and Photothermal Therapy for Ocular Treatments and Investigation of Corneal Endothelial Cell Migration
by Shadie Hatamie, Po-Jen Shih, Bo-Wei Chen, I-Jong Wang, Tai-Horng Young and Da-Jeng Yao
Nanomaterials 2020, 10(12), 2555; https://doi.org/10.3390/nano10122555 - 19 Dec 2020
Cited by 9 | Viewed by 3354
Abstract
The design of novel materials to use simultaneously in an ocular system for driven therapeutics and wound healing is still challenging. Here, we produced nanocomposites of tungsten disulfide carriers with spherical cobalt ferrite nanoparticles (NPs) as core inside a cubic iron oxide NPs [...] Read more.
The design of novel materials to use simultaneously in an ocular system for driven therapeutics and wound healing is still challenging. Here, we produced nanocomposites of tungsten disulfide carriers with spherical cobalt ferrite nanoparticles (NPs) as core inside a cubic iron oxide NPs shell (WS2/s-CoFe2O4@c-Fe3O4). Transmission electron microscopy (TEM) confirmed that 10 nm s-CoFe2O4@c-Fe3O4 NPs were attached on the WS2 sheet surfaces. The cytotoxicity of the WS2 sheets and nanocomposites were evaluated on bovine cornea endothelial cells (BCECs) using 3-(4,5-dimethylthiazol-2-yl)-2,5-diphenyltetrazolium bromide (MTT) assay for a duration of three days. The MTT assay results showed low toxicity of the WS2 sheets on BCECs by 67% cell viability at 100 μg/mL in 24 h, while the nanocomposites show 50% cell viability in the same conditions. The magnetic resonance imaging (MRI) of nanocomposites revealed the excellent T2-weighted imaging with an r2 contrast of 108 mM−1 S−1. The in vitro photothermal therapy based on WS2 sheets and WS2/s-CoFe2O4 @c-Fe3O4 nanocomposites using 808 nm laser showed that the maximum thermal energy dispatched in medium at different applied power densities (1200 mw, 1800, 2200, 2600 mW) was for 0.1 mg/mL of the sample solution. The migration assay of BCECs showed that the wound healing was approximately 20% slower for the cell exposed by nanocomposites compared with the control (no exposed BCECs). We believe that WS2/s-CoFe2O4@c-Fe3O4 nanocomposites have a synergic effect as photothermal therapy agents for eye diseases and could be a target in an ocular system using MRI. Full article
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<p>Transmission Electron Microscopy (TEM) images of the (<b>a</b>) WS<sub>2</sub> sheets, (<b>b</b>) s-CoFe<sub>2</sub>O<sub>4</sub>@c-Fe<sub>3</sub>O<sub>4</sub> NPs and (<b>c</b>) WS<sub>2</sub>/s-CoFe<sub>2</sub>O<sub>4</sub>@c-Fe<sub>3</sub>O<sub>4</sub> nanocomposites shows the layered structure of WS<sub>2</sub> and the size of the nanoparticles (NPs) is observed to be 10 nm, (<b>d</b>) the energy dispersive spectrometer (EDS) structural study of the s-CoFe<sub>2</sub>O<sub>4</sub>@c-Fe<sub>3</sub>O<sub>4</sub> NPs. The inset of figure (<b>c</b>) showed its corresponding selected area electron diffraction (SAED) pattern. (<b>d</b>) The EDS structural study of the s-CoFe<sub>2</sub>O<sub>4</sub>@ c-Fe<sub>3</sub>O<sub>4</sub> NPs confirmed the presence of the cobalt, iron and oxygen elements in the core-shell magnetic nanoparticles (MNPs).</p>
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<p>3-[4,5-dimethylthiazol-2yl]-2,5-diphenyl tetrazolium bromide (MTT) assay of the (<b>a</b>) WS<sub>2</sub> sheets and (<b>b</b>) WS<sub>2</sub>/s-CoFe<sub>2</sub>O<sub>4</sub>@c-Fe<sub>3</sub>O<sub>4</sub> nanocomposites on bovine cornea endothelial cells for duration of the 24, 48, and 72 h. The data were represented as mean ± SD (n = 3).</p>
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<p>(<b>a</b>) The cell migration scratching assay on bovine cornea endothelial cells (<b>b</b>) quantitative analysis of BCECs migration represent the relative wound width calculated in relation to initial time (0 h). Results are expressed as mean ± SD repeated n = 3 experiments.</p>
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<p>The photothermal evaluations of laser absorption of WS<sub>2</sub> sheets in various laser power densities of (<b>a</b>) 1200, (<b>b</b>) 1800, (<b>c</b>) 2200 and (<b>d</b>) 2600 mW at concentration 1, 0.5 and 0.1 mg/mL.</p>
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<p>The photothermal evaluations of laser absorption of WS<sub>2</sub>/CoFe<sub>2</sub>O<sub>4</sub> @Fe<sub>3</sub>O<sub>4</sub> nanocomposites in various laser power densities of (<b>a</b>) 1200, (<b>b</b>) 1800, (<b>c</b>) 2200 and (<b>d</b>) 2600 mW at concentration 1, 0.5, and 0.1 mg/mL.</p>
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<p>(<b>a</b>) T<sub>1</sub> and T<sub>2</sub>-weighted MR images at five different concentrations of nanocomposites. (<b>b</b>) The linear fitting of relaxation rates (1/T<sub>2</sub>) of versus nanocomposites concentrations. (<b>c</b>) The linear fitting of relaxation rates (1/T<sub>1</sub>) of versus nanocomposites concentrations. The relaxivity values of r<sub>2</sub> and r<sub>1</sub> were obtained from the slopes.</p>
Full article ">Scheme 1
<p>Shows the synthesis process of WS<sub>2</sub>/s-CoFe<sub>2</sub>O<sub>4</sub>@c-Fe<sub>3</sub>O<sub>4</sub> nanocomposites.</p>
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17 pages, 4499 KiB  
Article
Highly Sensitive Gas Sensing Material for Environmentally Toxic Gases Based on Janus NbSeTe Monolayer
by Deobrat Singh and Rajeev Ahuja
Nanomaterials 2020, 10(12), 2554; https://doi.org/10.3390/nano10122554 - 19 Dec 2020
Cited by 21 | Viewed by 3816
Abstract
Recently, a new family of the Janus NbSeTe monolayer has exciting development prospects for two-dimensional (2D) asymmetric layered materials that demonstrate outstanding properties for high-performance nanoelectronics and optoelectronics applications. Motivated by the fascinating properties of the Janus monolayer, we have studied the gas [...] Read more.
Recently, a new family of the Janus NbSeTe monolayer has exciting development prospects for two-dimensional (2D) asymmetric layered materials that demonstrate outstanding properties for high-performance nanoelectronics and optoelectronics applications. Motivated by the fascinating properties of the Janus monolayer, we have studied the gas sensing properties of the Janus NbSeTe monolayer for CO, CO2, NO, NO2, H2S, and SO2 gas molecules using first-principles calculations that will have eminent application in the field of personal security, protection of the environment, and various other industries. We have calculated the adsorption energies and sensing height from the Janus NbSeTe monolayer surface to the gas molecules to detect the binding strength for these considered toxic gases. In addition, considerable charge transfer between Janus monolayer and gas molecules were calculated to confirm the detection of toxic gases. Due to the presence of asymmetric structures of the Janus NbSeTe monolayer, the projected density of states, charge transfer, binding strength, and transport properties displayed distinct behavior when these toxic gases absorbed at Se- and Te-sites of the Janus monolayer. Based on the ultra-low recovery time in the order of ?s for NO and NO2 and ps for CO, CO2, H2S, and SO2 gas molecules in the visible region at room temperature suggest that the Janus monolayer as a better candidate for reusable sensors for gas sensing materials. From the transport properties, it can be observed that there is a significant variation of I?V characteristics and sensitivity of the Janus NbSeTe monolayer before and after adsorbing gas molecules demonstrates the feasibility of NbSeTe material that makes it an ideal material for a high-sensitivity gas sensor. Full article
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<p>(<b>a</b>) Optimized structure with top and side view, (<b>b</b>) projected density of states, (<b>c</b>) electronic band structure without spin-orbit coupling, and (<b>d</b>) electronic band structure with spin-orbit coupling of the Janus NbSeTe monolayer.</p>
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<p>Optimized structure of toxic gas molecules adsorbed on the surface of the Janus NbSeTe monolayer with the top and side view. (<b>a</b>) CO, (<b>b</b>) CO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>c</b>) NO, (<b>d</b>) NO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>e</b>) H<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>S, and (<b>f</b>) SO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math> gas molecules adsorbed on Se-side of the Janus NbSeTe monolayer.</p>
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<p>Optimized structure of toxic gas molecules adsorbed on the surface of the Janus NbSeTe monolayer with the top and side view. (<b>a</b>) CO, (<b>b</b>) CO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>c</b>) NO, (<b>d</b>) NO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>e</b>) H<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>S, and (<b>f</b>) SO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math> gas molecules adsorbed on the Te-side of the Janus NbSeTe monolayer.</p>
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<p>Projected density of states (PDOS) influenced by the toxic gas molecules adsorbed on the surface of the Janus NbSeTe monolayer with top and side view. (<b>a</b>) CO, (<b>b</b>) CO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>c</b>) NO, (<b>d</b>) NO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>e</b>) H<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>S, and (<b>f</b>) SO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math> gas molecules adsorbed on the Se-side of the Janus NbSeTe monolayer.</p>
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<p>Projected density of states (PDOS) influenced by the toxic gas molecules adsorbed on the surface of the Janus NbSeTe monolayer with top and side view. (<b>a</b>) CO, (<b>b</b>) CO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>c</b>) NO, (<b>d</b>) NO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, (<b>e</b>) H<math display="inline"><semantics> <mrow> <msub> <mrow/> <mn>2</mn> </msub> </mrow> </semantics></math>S, and (<b>f</b>) SO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math> gas molecules adsorbed on the Te-side of the Janus NbSeTe monolayer.</p>
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<p>(<b>a</b>) Schematic representation of the device model constituted by three parts: the semi-infinite left (L) and right (R) electrodes and scattering region. Current–voltage characteristics of the Janus NbSeTe monolayer for (<b>b</b>) gas molecules absorbed on the Se-side and (<b>c</b>) gas molecules absorbed on the Te-side.</p>
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<p>Transmission spectra of the Janus NbSeTe monolayer for (<b>a</b>) gas molecules absorbed on the Se-side and (<b>b</b>) gas molecules absorbed on the Te-side.</p>
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<p>The sensitivity of CO, CO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, NO, NO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>, H<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math>S, and SO<math display="inline"><semantics> <msub> <mrow/> <mn>2</mn> </msub> </semantics></math> gas molecules on the surface of the Janus NbSeTe monolayer at a voltage of 0.3 V.</p>
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15 pages, 4408 KiB  
Article
Role of Thermodynamics and Kinetics in the Composition of Ternary III-V Nanowires
by Egor D. Leshchenko and Jonas Johansson
Nanomaterials 2020, 10(12), 2553; https://doi.org/10.3390/nano10122553 - 18 Dec 2020
Cited by 11 | Viewed by 2291
Abstract
We explain the composition of ternary nanowires nucleating from a quaternary liquid melt. The model we derive describes the evolution of the solid composition from the nucleated-limited composition to the kinetic one. The effect of the growth temperature, group V concentration and Au/III [...] Read more.
We explain the composition of ternary nanowires nucleating from a quaternary liquid melt. The model we derive describes the evolution of the solid composition from the nucleated-limited composition to the kinetic one. The effect of the growth temperature, group V concentration and Au/III concentration ratio on the solid-liquid dependence is studied. It has been shown that the solid composition increases with increasing temperature and Au concentration in the droplet at the fixed In/Ga concentration ratio. The model does not depend on the site of nucleation and the geometry of monolayer growth and is applicable for nucleation and growth on a facet with finite radius. The case of a steady-state (or final) solid composition is considered and discussed separately. While the nucleation-limited liquid-solid composition dependence contains the miscibility gap at relevant temperatures for growth of InxGa1−xAs NWs, the miscibility gap may be suppressed completely in the steady-state growth regime at high supersaturation. The theoretical results are compared with available experimental data via the combination of the here described solid-liquid and a simple kinetic liquid-vapor model. Full article
(This article belongs to the Special Issue Preparation and Application of Nanowires)
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<p>Schematic illustration of the system.</p>
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<p>Dependence of the steady-state solid composition on the liquid composition for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs and contour plots of chemical potential differences between the species AD (<b>a</b>) and BD (<b>b</b>) in the liquid phase and the solid phase. Dashed lines indicate miscibility gaps.</p>
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<p>Dependence of the steady-state solid composition on the liquid composition for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs and contour plots of chemical potential differences between the species AD (<b>a</b>) and BD (<b>b</b>) in the liquid phase and the solid phase. Dashed lines indicate miscibility gaps.</p>
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<p>Dependence of the steady-state solid composition on the liquid composition for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs. Solid lines and circles correspond to Equations (8) and (20), respectively. Dashed line indicates miscibility gap.</p>
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<p>Evolution of the solid composition with nucleus size for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs at <math display="inline"><semantics> <mrow> <mi>y</mi> <mo>=</mo> <mn>0.96</mn> </mrow> </semantics></math>. The solid thin lines correspond to the levels of the formation energy, <span class="html-italic">F</span>.</p>
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<p>Numerical (circles) and analytical (solid) evolution of the liquid-solid dependence of In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs with the size (<math display="inline"><semantics> <mrow> <mi>δ</mi> <mo>=</mo> <mn>1</mn> <mo>,</mo> <mtext> </mtext> <mn>0.71</mn> <mo>,</mo> <mtext> </mtext> <mn>0.44</mn> <mo>,</mo> <mtext> </mtext> <mn>0.10</mn> <mo>,</mo> <mtext> </mtext> <mn>0</mn> </mrow> </semantics></math>) at <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>400</mn> </mrow> </semantics></math> °C, <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>s</mi> </mrow> </msub> <mtext> </mtext> <mo>=</mo> <mtext> </mtext> <mn>0.02</mn> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>u</mi> </mrow> </msub> <mtext> </mtext> <mo>=</mo> <mtext> </mtext> <mn>0.1</mn> </mrow> </semantics></math>. Blue solid and ginger dash-dotted curves correspond to nucleation limited and kinetic composition dependencies respectively. Dashed lines indicate miscibility gaps.</p>
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<p>Liquid-solid composition dependences for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>As NWs at fixed <math display="inline"><semantics> <mrow> <mi>K</mi> <mo>=</mo> <mn>1</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>s</mi> </mrow> </msub> <mo>=</mo> <mn>0.01</mn> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mi>δ</mi> <mo>=</mo> <mn>0.38</mn> <mo>,</mo> <mtext> </mtext> <mn>1</mn> </mrow> </semantics></math> (<b>a</b>) for different temperatures at fixed <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>u</mi> </mrow> </msub> <mo>=</mo> <mn>0.4</mn> </mrow> </semantics></math> and (<b>b</b>) for different Au/III concentration ratios at fixed <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>400</mn> </mrow> </semantics></math> °C.</p>
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<p>Chemical potential difference between the liquid and solid for different Sb concentrations in the liquid (<math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>S</mi> <mi>b</mi> </mrow> </msub> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math> (<b>a</b>) and <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>S</mi> <mi>b</mi> </mrow> </msub> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math> (<b>b</b>)) and liquid-solid composition dependences of In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>Sb NWs (<b>c</b>) at fixed Au concentration <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>u</mi> </mrow> </msub> <mo>=</mo> <mn>0.2</mn> </mrow> </semantics></math> and temperature <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>450</mn> </mrow> </semantics></math> °C. For better clarity, only the positive values of the chemical potential difference are presented. Negative values are shown as level 0 (dark blue).</p>
Full article ">Figure 7 Cont.
<p>Chemical potential difference between the liquid and solid for different Sb concentrations in the liquid (<math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>S</mi> <mi>b</mi> </mrow> </msub> <mo>=</mo> <mn>0.1</mn> </mrow> </semantics></math> (<b>a</b>) and <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>S</mi> <mi>b</mi> </mrow> </msub> <mo>=</mo> <mn>0.3</mn> </mrow> </semantics></math> (<b>b</b>)) and liquid-solid composition dependences of In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>Sb NWs (<b>c</b>) at fixed Au concentration <math display="inline"><semantics> <mrow> <msub> <mi>c</mi> <mrow> <mi>A</mi> <mi>u</mi> </mrow> </msub> <mo>=</mo> <mn>0.2</mn> </mrow> </semantics></math> and temperature <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>450</mn> </mrow> </semantics></math> °C. For better clarity, only the positive values of the chemical potential difference are presented. Negative values are shown as level 0 (dark blue).</p>
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<p>Theoretical (steady-state) and experimental vapor-solid composition dependences for In<span class="html-italic"><sub>x</sub></span>Ga<sub>1−<span class="html-italic">x</span></sub>Sb NWs for different temperatures. The stars represent experimental data from [<a href="#B36-nanomaterials-10-02553" class="html-bibr">36</a>]; the rest of the experimental data (squares and circles) are obtained from [<a href="#B35-nanomaterials-10-02553" class="html-bibr">35</a>].</p>
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15 pages, 5395 KiB  
Article
Organic–Inorganic Ternary Nanohybrids of Single-Walled Carbon Nanohorns for Room Temperature Chemiresistive Ethanol Detection
by Cornel Cobianu, Bogdan-Catalin Serban, Niculae Dumbravescu, Octavian Buiu, Viorel Avramescu, Cristina Pachiu, Bogdan Bita, Marius Bumbac, Cristina-Mihaela Nicolescu and Cosmin Cobianu
Nanomaterials 2020, 10(12), 2552; https://doi.org/10.3390/nano10122552 - 18 Dec 2020
Cited by 20 | Viewed by 2896
Abstract
Organic–inorganic ternary nanohybrids consisting of oxidized-single walled carbon nanohorns-SnO2-polyvinylpyrrolidone (ox-SWCNH/SnO2/PVP) with stoichiometry 1/1/1 and 2/1/1 and ox-SWCNH/ZnO/PVP = 5/2/1 and 5/3/2 (all mass ratios) were synthesized and characterized as sensing films of chemiresistive test structures for ethanol vapor detection [...] Read more.
Organic–inorganic ternary nanohybrids consisting of oxidized-single walled carbon nanohorns-SnO2-polyvinylpyrrolidone (ox-SWCNH/SnO2/PVP) with stoichiometry 1/1/1 and 2/1/1 and ox-SWCNH/ZnO/PVP = 5/2/1 and 5/3/2 (all mass ratios) were synthesized and characterized as sensing films of chemiresistive test structures for ethanol vapor detection in dry air, in the range from 0 up to 50 mg/L. All the sensing films had an ox-SWCNH concentration in the range of 33.3–62.5 wt%. A comparison between the transfer functions and the response and recovery times of these sensing devices has shown that the structures with ox-SWCNH/SnO2/PVP = 1/1/1 have the highest relative sensitivities of 0.0022 (mg/L)−1, while the devices with ox-SWCNH/SnO2/PVP = 2/1/1 have the lowest response time (15 s) and recovery time (50 s) for a room temperature operation, proving the key role of carbonic material in shaping the static and dynamic performance of the sensor. These response and recovery times are lower than those of “heated” commercial sensors. The sensing mechanism is explained in terms of the overall response of a p-type semiconductor, where ox-SWCNH percolated between electrodes of the sensor, shunting the heterojunctions made between n-type SnO2 or ZnO and p-type ox-SWCNH. The hard–soft acid–base (HSAB) principle supports this mechanism. The low power consumption of these devices, below 2 mW, and the sensing performances at room temperature may open new avenues towards ethanol sensors for passive samplers of environment monitoring, alcohol test portable instruments and wireless network sensors for Internet of Things applications. Full article
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Figure 1
<p>Raman spectra of solid-state films of single walled carbon nanohorns-SnO<sub>2</sub>-polyvinylpyrrolidone (SWCNH/SnO<sub>2</sub>/PVP) = 1/1/1 (mass ratio) deposited on silicon substrate.</p>
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<p>SEM images of the sensing ternary films deposited on the sensing area of the test structure. (<b>a</b>) Oxidized-single walled carbon nanohorns-SnO<sub>2</sub>-polyvinylpyrrolidone (ox-SWCNH/SnO<sub>2</sub>/PVP) = 1/1/1; (<b>b</b>) and ox-SWCNH/SnO<sub>2</sub> = 2/1/1.</p>
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<p>Transfer functions of the chemiresistive ethanol sensors with sensing films kept at room temperature and consisting of (<b>a</b>) ox-SWCNH/SnO<sub>2</sub>/PVP = 1/1/1 (mass ratio) and (<b>b</b>) ox-SWCNH/SnO<sub>2</sub>/PVP = 2/1/1 (mass ratio). For both cases, the flow rate of air passing through liquid ethanol was varied, while the total flow rate was kept constant at 1 L/min. The inset shows the automatic recording of the sensor resistance as a function of time and ethanol vapor concentration.</p>
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<p>Transfer functions of the chemiresistive ethanol sensors with sensing films kept at room temperature and consisting of (<b>a</b>) ox-SWCNH/ZnO/PVP = 5/2/1 (mass ratio) and (<b>b</b>) ox-SWCNH/ZnO/PVP = 5/3/2. For both cases, the flow rate of air passing through liquid ethanol was varied, while the total flow rate was kept constant at 1 L/min. The inset shows the automatic recording of the sensor resistance as a function of time and ethanol vapor concentration.</p>
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<p>Response and the recovery times of the chemiresistive ethanol sensors with sensing films kept at room temperature and consisting of (<b>a</b>) ox-SWCNH/SnO<sub>2</sub>/PVP = 1/1/1 (mass ratio), where (<b>a1</b>) is response time, and (<b>a2</b>) is recovery time and (<b>b</b>) ox-SWCNH/SnO<sub>2</sub>/PVP = 2/1/1 (mass ratio), where (<b>b1</b>) is response time, and (<b>b2</b>) is recovery time. Response time was measured for a change in ethanol vapor concentration from 2 to 5 mg/L, while the recovery time was measured for a change in ethanol vapor concentration from 25 mg/L to 0 mg/L. For both cases, the flow rate of air passing through liquid ethanol was varied, while the total flow rate in the test chamber was kept constant at 1 L/min.</p>
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<p>Response and recovery times of the chemiresistive ethanol sensors with sensing films kept at room temperature and consisting of (<b>a</b>) ox-SWCNH/ZnO/PVP = 5/2/1 (mass ratio); (<b>a1</b>) response time, and (<b>a2</b>) recovery time, and (<b>b</b>) ox-SWCNH/ZnO/PVP = 5/3/2 (mass ratio); (<b>b1</b>) response time, and (<b>b2</b>) recovery time. Response time was measured for a change in ethanol vapor concentration from 2 to 5 mg/L, while the recovery time was measured for a change in ethanol vapor concentration from 25 mg/L to 0 mg/L. For both cases, the flow rate of air passing through liquid ethanol was varied, while the total flow rate was kept constant at 1 L/min.</p>
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24 pages, 4626 KiB  
Article
An Organic–Inorganic Hybrid Nanocomposite as a Potential New Biological Agent
by Mateusz Dulski, Katarzyna Malarz, Michał Kuczak, Karolina Dudek, Krzysztof Matus, Sławomir Sułowicz, Anna Mrozek-Wilczkiewicz and Anna Nowak
Nanomaterials 2020, 10(12), 2551; https://doi.org/10.3390/nano10122551 - 18 Dec 2020
Cited by 9 | Viewed by 3246 | Correction
Abstract
To solve the problem of human diseases caused by a combination of genetic and environmental factors or by microorganisms, intense research to find completely new materials is required. One of the promising systems in this area is the silver-silica nanocomposites and their derivatives. [...] Read more.
To solve the problem of human diseases caused by a combination of genetic and environmental factors or by microorganisms, intense research to find completely new materials is required. One of the promising systems in this area is the silver-silica nanocomposites and their derivatives. Hence, silver and silver oxide nanoparticles that were homogeneously distributed within a silica carrier were fabricated. Their average size was d = (7.8 ± 0.3) nm. The organic polymers (carboxymethylcellulose (CMC) and sodium alginate (AS)) were added to improve the biological features of the nanocomposite. The first system was prepared as a silver chlorine salt combination that was immersed on a silica carrier with coagulated particles whose size was d = (44.1 ± 2.3) nm, which coexisted with metallic silver. The second system obtained was synergistically interacted metallic and oxidized silver nanoparticles that were distributed on a structurally defective silica network. Their average size was d = (6.6 ± 0.7) nm. Physicochemical and biological experiments showed that the tiny silver nanoparticles in Ag/SiO2 and Ag/SiO2@AS inhibited E. coli, P. aeruginosa, S. aureus, and L. plantarum’s cell growth as well as caused a high anticancer effect. On the other hand, the massive silver nanoparticles of Ag/SiO2@CMC had a weaker antimicrobial effect, although they highly interacted against PANC-1. They also generated reactive oxygen species (ROS) as well as the induction of apoptosis via the p53-independent mechanism. Full article
(This article belongs to the Special Issue Hybrid Nanomaterials Synthesis and Application)
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<p>Two synthesis routes (<b>A</b>,<b>B</b>) were considered to fabricate the powder (<b>A</b>) silver-silica nanocomposite and (<b>B</b>) its derivatives.</p>
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<p>XRD pattern of (<b>a</b>) initial Ag/SiO<sub>2</sub> powder and modified systems by (<b>b</b>) carboxymethylcellulose: Ag/SiO<sub>2</sub>@CMC and (<b>c</b>) sodium alginate: Ag/SiO<sub>2</sub>@AS with the Rietveld refinement (red line).</p>
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<p>The Raman spectra of the silver-silica (Ag/SiO<sub>2</sub>) and modified nanocomposites through carboxymethylcellulose (Ag/SiO<sub>2</sub>@CMC) and sodium alginate (Ag/SiO<sub>2</sub>@AS) were in the 120–1800 cm <sup>−1</sup> region. Additionally, to better illustrate the silica matrix signal, the 350–1100 cm<sup>−1</sup> region in Ag/SiO<sub>2</sub>@CMC was magnified 10×. Each spectrum was fitted using the Voigt function and a minimum number of components.</p>
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<p>Backscattered electron (BSE)-SEM (<b>a</b>–<b>c</b>) images present the morphology of (<b>a</b>) Ag/SiO<sub>2</sub>, (<b>b</b>) Ag/SiO<sub>2</sub>@CMC, (<b>c</b>) Ag/SiO<sub>2</sub>@AS and the SEM-energy dispersive spectrometer (EDS) chemical composition maps of the (<b>d</b>) Ag/SiO<sub>2</sub>, (<b>e</b>) Ag/SiO<sub>2</sub>@CMC, and (<b>f</b>) Ag/SiO<sub>2</sub>@AS nanocomposites and their derivatives. The small insets highlight the individual elemental distribution maps of Ag (yellow), Si (red), O (blue), and Cl (green) from the EDS. CMC means carboxymethylcellulose, while AS refers to sodium alginate.</p>
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<p>High resolution transmision electron microscopy (HRTEM) images of (<b>a</b>) the pure silver-silica nanocomposite and the chemically modified silver-silica derivatives; (<b>b</b>) Ag/SiO<sub>2</sub>@CMC and (<b>c</b>) Ag/SiO<sub>2</sub>@AS with an inset showing the selected area electron diffraction (SAED) patterns for Ag and the size distribution of Ag fitted by the Gaussian function.</p>
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<p>The XPS spectra of (<b>a</b>) Ag 3d, (<b>b</b>) Si 2p, (<b>c</b>) O 1s, and (<b>d</b>) the C 1s core levels with the fitting result. The individual colors on the specific lines’ core levels refer to the individual chemical surroundings linked to the silver, silica, oxygen, and carbon.</p>
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<p>The XPS spectrum of the Cl 2p core level with the result of the fitting for Ag/SiO<sub>2</sub>@CMC.</p>
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<p>The ability of the Gram-negative (<span class="html-italic">Escherichia coli, Pseudomonas aeruginosa</span>), Gram-positive bacteria (<span class="html-italic">Lactobacillus plantarum</span>, <span class="html-italic">Staphylococcus aureus)</span> and yeast strains (<span class="html-italic">Candida albicans</span>, <span class="html-italic">Saccharomyces cerevisiae</span>) to form a colony after a 24 h exposure to the Ag/SiO<sub>2</sub>, Ag/SiO<sub>2</sub>@CMC, Ag/SiO<sub>2</sub>@AS, and Ag<sup>+</sup>-ions (reference). After exposure, the cells (5 µL) were transferred onto a toxicant-free agarized growth medium. The lowest concentration (mg/L), providing total microbial growth inhibition was considered minimum biocidal concentration (MBC).</p>
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<p>Impact of the tested nanocomposites at a 30 mg/L concentration on regulating the cell cycle (<b>a</b>) and inducing apoptosis (<b>b</b>) in the PANC-1 cells. Effect of the tested Ag/SiO<sub>2</sub>@CMC nanocomposite on the level of reactive oxygen species (ROS) in the PANC-1 cells. Data normalized to the untreated cells (control) (<b>c</b>). Impact of Ag/SiO<sub>2</sub>@CMC on the expression of the p53, cyclin E1, and HO-1 proteins in the PANC-1 cells. The densitometric analysis of these proteins was normalized to GADPH (<b>d</b>). The results from all experiments are shown as the mean ± standard deviation (SD) of three independent measurements. Any statistical differences from the cell cycle, apoptosis, and immunoblotting experiments were analyzed using a one-way ANOVA with Bonferroni’s <span class="html-italic">post-hoc</span> test. Data from ROS measurements were analyzed using the Student’s <span class="html-italic">t</span>-test. Statistical significance: * <span class="html-italic">p</span> &lt; 0.05, ** <span class="html-italic">p</span> &lt; 0.01, *** <span class="html-italic">p</span> &lt; 0.001, **** <span class="html-italic">p</span> &lt; 0.0001 compared to the control group.</p>
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20 pages, 6222 KiB  
Article
Cytotoxicity and Bioimaging Study for NHDF and HeLa Cell Lines by Using Graphene Quantum Pins
by Seong-Beom Jeon, Monica Samal, Saravanan Govindaraju, Rupasree Ragini Das and Kyusik Yun
Nanomaterials 2020, 10(12), 2550; https://doi.org/10.3390/nano10122550 - 18 Dec 2020
Cited by 4 | Viewed by 2977
Abstract
Herein, we report the synthesis of an interesting graphene quantum material called “graphene quantum pins (GQPs)”. Morphological analysis revealed the interesting pin shape (width: ~10 nm, length: 50–100 nm) and spectral analysis elucidated the surface functional groups, structural features, energy levels, and photoluminescence [...] Read more.
Herein, we report the synthesis of an interesting graphene quantum material called “graphene quantum pins (GQPs)”. Morphological analysis revealed the interesting pin shape (width: ~10 nm, length: 50–100 nm) and spectral analysis elucidated the surface functional groups, structural features, energy levels, and photoluminescence properties (blue emission under 365 nm). The difference between the GQPs and graphene quantum dos (GQDs) isolated from the same reaction mixture as regards to their morphological, structural, and photoluminescence properties are also discussed along with the suggestion of a growth mechanism. Cytotoxicity and cellular responses including changes in biophysical and biomechanical properties were evaluated for possible biomedical applications of GQPs. The studies demonstrated the biocompatibility of GQPs even at a high concentration of 512 μg/mL. Our results suggest GQPs can be used as a potential bio-imaging agent with desired photoluminescence property and low cytotoxicity. Full article
(This article belongs to the Section 2D and Carbon Nanomaterials)
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<p>HR-TEM image and AFM image of (<b>A</b>,<b>B</b>) graphene quantum dos (GQDs) and (<b>C</b>,<b>D</b>) Graphene Quantum Pins (GQPs). The scale bars, 50 nm (<b>A</b>,<b>C</b>), 5 nm (inset). HR-TEM images are shown in inset image. (<b>B</b>,<b>D</b>) The AFM image show some aggregation of GQDs and GQPs due to electrostatic attraction. The maximum heights are 4.92 nm, 68.3 nm for GQDs and GQPs, respectively.</p>
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<p>The results of XPS show a clear difference of functional groups on GQPs and GQDs surface. The spectrum of C1s in (<b>A</b>) GQPs and (<b>D</b>) GQDs can be categorized into 4 groups. The peak intensity is significantly reduced for the COOH group in GQPs with also a visible decrease in the C–O–C intensity. The N1s and Cl2p spectrums of (<b>B</b>,<b>C</b>) GQPs and (<b>E</b>,<b>F</b>) GQDs show nitrogen and chloride doping and the presence of tertiary amine.</p>
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<p>Spectral analysis of obtained GQPs and GQDs. (<b>A</b>) FT-IR spectroscopy, (<b>B</b>) UV-vis spectroscopy, (<b>C</b>) Raman Spectroscopy.</p>
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<p>(<b>A</b>) Normalized photoluminescence emission (PL), photoluminescence excitation (PLE) spectra of GQPs and GQDs. (<b>B</b>) Optical transition for GQPs and typical Fluorescence spectra of obtained (<b>C</b>) GQDs and (<b>D</b>) GQPs (Inset: Under visible (left) and under 365 nm UV radiation (right)).</p>
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<p>(<b>A</b>) Ultraviolet photoelectron spectroscopy (UPS) spectra (<b>B</b>) Fermi energy, a work function of GQPs (taking gold as standard).</p>
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<p>Toxicity of GQDs and GQPs in (<b>A</b>) normal human dermal fibroblast (NHDF) and (<b>B</b>) HeLa. Cell viability of GQDs and GQPs measured using CCK-8 assay. Experiments were repeated thrice with the triplicate, and significant difference between control and test samples are marked with ** (<span class="html-italic">p</span> &lt; 0.01), and *** (<span class="html-italic">p</span> &lt; 0.001). ROS generation level of GQDs and GQPs in (<b>C</b>) NHDF and (<b>D</b>) HeLa. The level of GQDs and GQPs measured using DCFH-DA assay. Experiments were repeated thrice with the triplicate, and a significant difference between control and test samples are satisfied in all test concentrations.</p>
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<p>AFM image of cells after treatment of GQDs and GQPs. AFM 3D images of control cells; (<b>A</b>) NHDF, (<b>D</b>) HeLa. In the case of NHDF, compared to the control, the cell surface became much rougher when the cells were treated with (<b>B</b>) GQDs and broader when the cells were treated with (<b>C</b>) GQPs. The pores and blebs, which indicate cell apoptosis, were found to be larger upon cell treatment with GQDs and GQPs, as compared to the control group. In the case of HeLa, no specific change in cell shape was observed, but the blebs on the surface were more obvious after treatment with (<b>E</b>) GQDs than after treatment with (<b>F</b>) GQPs.</p>
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<p>Quantitative analysis of cellular responses upon treatment with GQDs and GQPs in NHDF and HeLa. Graphs show (<b>A</b>,<b>E</b>) average cell height, (<b>B</b>,<b>F</b>) RMS roughness, (<b>C</b>,<b>G</b>) cell spreading area and (<b>D</b>,<b>H</b>) stiffness of cells, respectively. Experiments were repeated thrice with triplicate and significant differences between control and test samples are marked with * (<span class="html-italic">p</span> &lt; 0.05), ** (<span class="html-italic">p</span> &lt; 0.01), and *** (<span class="html-italic">p</span> &lt; 0.001).</p>
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<p>Bio-imaging of GQDs and GQPs in NHDF. Fluorescence emission of both GQDs increased with increasing incubation time. Each scale bar (yellow bar) was 100 μm.</p>
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<p>3D reconstructed confocal images for analysis of cellular distribution of GQDs and GQPs in NHDF. The fluorescence emission was present only in cytoplasm except nucleus until 12 h. After 24 h, it was observed in the whole cell. The two images at the bottom of figure were the 3D reconstructed confocal images of blocking endocytosis at low temperature. X and <span class="html-italic">Y</span>-axis scale are 100 μm and the yellow line indicates the cross-section of confocal image.</p>
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<p>The growth mechanism of GQPs from glucose.</p>
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15 pages, 3090 KiB  
Article
Eco-Friendly 1,3-Dipolar Cycloaddition Reactions on Graphene Quantum Dots in Natural Deep Eutectic Solvent
by Salvatore V. Giofrè, Matteo Tiecco, Consuelo Celesti, Salvatore Patanè, Claudia Triolo, Antonino Gulino, Luca Spitaleri, Silvia Scalese, Mario Scuderi and Daniela Iannazzo
Nanomaterials 2020, 10(12), 2549; https://doi.org/10.3390/nano10122549 - 18 Dec 2020
Cited by 35 | Viewed by 3743
Abstract
Due to their outstanding physicochemical properties, the next generation of the graphene family—graphene quantum dots (GQDs)—are at the cutting edge of nanotechnology development. GQDs generally possess many hydrophilic functionalities which allow their dispersibility in water but, on the other hand, could interfere with [...] Read more.
Due to their outstanding physicochemical properties, the next generation of the graphene family—graphene quantum dots (GQDs)—are at the cutting edge of nanotechnology development. GQDs generally possess many hydrophilic functionalities which allow their dispersibility in water but, on the other hand, could interfere with reactions that are mainly performed in organic solvents, as for cycloaddition reactions. We investigated the 1,3-dipolar cycloaddition (1,3-DCA) reactions of the C-ethoxycarbonyl N-methyl nitrone 1a and the newly synthesized C-diethoxyphosphorylpropilidene N-benzyl nitrone 1b with the surface of GQDs, affording the isoxazolidine cycloadducts isox-GQDs 2a and isox-GQDs 2b. Reactions were performed in mild and eco-friendly conditions, through the use of a natural deep eutectic solvent (NADES), free of chloride or any metal ions in its composition, and formed by the zwitterionic trimethylglycine as the -bond acceptor, and glycolic acid as the hydrogen-bond donor. The results reported in this study have for the first time proved the possibility of performing cycloaddition reactions directly to the p-cloud of the GQDs surface. The use of DES for the cycloaddition reactions on GQDs, other than to improve the solubility of reactants, has been shown to bring additional advantages because of the great affinity of these green solvents with aromatic systems. Full article
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<p>Eco-friendly synthesis of <span class="html-italic">isox</span>-graphene quantum dots (GQDs) <b>2a,b</b> by 1,3-DCA reactions in natural deep eutectic solvent (NADES) medium.</p>
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<p>(<b>a</b>) Representative HRTEM image of a GQDs cluster with mean particle size of 4.8 nm and the corresponding fast Fourier transform (FTT) on the inset showing planes at 0.21 nm; (<b>b</b>) DLS measurement of GQDs dispersion in deionized water; (<b>c</b>) optical properties of GQDs dispersions in deionized water: UV—vis absorption spectrum of GQDs (blue line) and photoluminescence (PL) spectrum of GQDs at the excitation wavelengths of 360 nm (red line).</p>
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<p>(<b>a</b>) TGA curves of GQDs, <span class="html-italic">isox</span>-GQDs <b>2a</b> and <span class="html-italic">isox</span>-GQDs <b>2b</b>, performed in Ar atmosphere; (<b>b</b>) FTIR spectra of GQDs, <span class="html-italic">isox</span>-GQDs <b>2a</b> and <span class="html-italic">isox</span>-GQDs <b>2b</b>.</p>
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<p>Al-Kα excited XPS of: (<b>a</b>,<b>b</b>) <span class="html-italic">isox</span>-GQDs <b>2a</b> in the C 1s and O 1s binding energy regions; (<b>c</b>) overlapped XPS of the <span class="html-italic">isox</span>-GQDs <b>2b</b> (black line) and <span class="html-italic">isox</span>-GQDs <b>2a</b> (red line) in the N 1s binding energy region; (<b>d</b>,<b>e</b>) <span class="html-italic">isox</span>-GQDs <b>2b</b> in the C 1s and O 1s binding energy regions; (<b>f</b>) <span class="html-italic">isox</span>-GQDs 2b in the P 2p binding energy region.</p>
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<p>PL spectra of GQDs, <span class="html-italic">isox</span>-GQDs <b>2a</b> and <span class="html-italic">isox</span>-GQDs <b>2b</b>, at the λ<sub>exc</sub> of 360 nm. All samples were tested at a concentration of 100 ng/mL.</p>
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<p>Raman spectra of: (<b>a</b>) GQDs, (<b>b</b>) <span class="html-italic">isox</span>-GQDs <b>2a</b> and (<b>c</b>) <span class="html-italic">isox</span>-GQDs <b>2b</b>.</p>
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<p>(<b>a</b>) Atomic force microscopy (AFM) image of the GQDs deposited on the Si substrate and (<b>b</b>) line profile referring to the green line in figure (<b>a</b>); (<b>c</b>) AFM image of <span class="html-italic">isox</span>-GQDs <b>2a</b> deposited on the Si substrate and (<b>d</b>) line profile referring to the green line in (<b>c</b>); (<b>e</b>) AFM image of <span class="html-italic">isox</span>-GQDs <b>2b</b> deposited on the Si substrate and (<b>f</b>) line profile referring to the green line in (<b>e</b>).</p>
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<p>Synthesis of cycloadducts <span class="html-italic">isox</span>-GQDs <b>2a</b> and <span class="html-italic">isox</span>-GQDs <b>2b</b>. Reagents and conditions: GA/TMG (2:1 molar ratio), MW, 1 h, 90 °C, 150 W.</p>
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15 pages, 5738 KiB  
Article
Effect of Water and Glycerol in Deoxygenation of Coconut Oil over Bimetallic NiCo/SAPO-11 Nanocatalyst under N2 Atmosphere
by Rungnapa Kaewmeesri, Jeeranan Nonkumwong, Thongthai Witoon, Navadol Laosiripojana and Kajornsak Faungnawakij
Nanomaterials 2020, 10(12), 2548; https://doi.org/10.3390/nano10122548 - 18 Dec 2020
Cited by 3 | Viewed by 2757
Abstract
The catalytic deoxygenation of coconut oil was performed in a continuous-flow reactor over bimetallic NiCo/silicoaluminophosphate-11 (SAPO-11) nanocatalysts for hydrocarbon fuel production. The conversion and product distribution were investigated over NiCo/SAPO-11 with different applied co-reactants, i.e., water (H2O) or glycerol solution, performed [...] Read more.
The catalytic deoxygenation of coconut oil was performed in a continuous-flow reactor over bimetallic NiCo/silicoaluminophosphate-11 (SAPO-11) nanocatalysts for hydrocarbon fuel production. The conversion and product distribution were investigated over NiCo/SAPO-11 with different applied co-reactants, i.e., water (H2O) or glycerol solution, performed under nitrogen (N2) atmosphere. The hydrogen-containing co-reactants were proposed here as in-situ hydrogen sources for the deoxygenation, while the reaction tests under hydrogen (H2) atmosphere were also applied as a reference set of experiments. The results showed that applying co-reactants to the reaction enhanced the oil conversion as the following order: N2 (no co-reactant) < N2 (H2O) < N2 (aqueous glycerol) < H2 (reference). The main products formed under the existence of H2O or glycerol solution were free fatty acids (FFAs) and their corresponding Cn−1 alkanes. The addition of H2O aids the triglyceride breakdown into FFAs, whereas the glycerol acts as hydrogen donor which is favourable to initiate hydrogenolysis of triglycerides, causing higher amount of FFAs than the former case. Consequently, those FFAs can be deoxygenated via decarbonylation/decarboxylation to their corresponding Cn−1 alkanes, showing the promising capability of the NiCo/SAPO-11 to produce hydrocarbon fuels even in the absence of external H2 source. Full article
(This article belongs to the Special Issue Nanotechnologies and Nanomaterials: Selected Papers from CCMR)
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<p>Schematic diagram of continuous-flow reactor system for catalytic testing.</p>
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<p>(<b>a</b>) XRD patterns, * 2θ = 44.41°, 51.78°, and 76.09° (powder diffraction file (PDF) for Ni-Co alloy (01-074-5694)); (<b>b</b>) N<sub>2</sub> adsorption-desorption isotherms; and (<b>c</b>) pore-size distributions of SAPO-11 and the reduced NiCo/SAPO-11 catalyst.</p>
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<p>(<b>a</b>) Scanning electron microscopy (SEM) image; (<b>b</b>) transmission electron microscopy (TEM) image; (<b>c</b>,<b>d</b>) corresponding energy dispersive X-ray spectrometer (EDS) elemental mappings of Ni and Co; (<b>e</b>,<b>f</b>) EDS line profile of the NiCo/SAPO-11 catalyst.</p>
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<p>Oil conversion and product yield of coconut oil deoxygenation under different atmospheres with (w/) and without (w/o) co-reactant feeds. (Condition: Coconut oil, LHSV of 1 h<sup>−1</sup>, 330 °C, and 50 bar of reaction gas, Gly = glycerol solution).</p>
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<p>Distribution of liquid hydrocarbon products of coconut oil deoxygenation under different atmospheres with (w/) and without (w/o) co-reactant feeds. (Condition: Coconut oil, LHSV of 1 h<sup>−1</sup>, 330 °C, and 50 bar of reaction gas, Gly = glycerol solution).</p>
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<p>Distribution of gas species of coconut oil deoxygenation under different atmospheres with (w/) and without (w/o) co-reactant feeds. (Condition: Coconut oil, LHSV of 1 h<sup>−1</sup>, 330 °C, and 50 bar of reaction gas, Gly = glycerol solution).</p>
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10 pages, 4352 KiB  
Article
Direct Laser Writing of Transparent Polyimide Film for Supercapacitor
by Fei Huang, Guoying Feng, Jiajia Yin, Sikun Zhou, Li Shen, Shutong Wang and Yun Luo
Nanomaterials 2020, 10(12), 2547; https://doi.org/10.3390/nano10122547 - 18 Dec 2020
Cited by 21 | Viewed by 4143
Abstract
Direct laser writing (DLW) is a convenient approach for fabricating graphene-based flexible electronic devices. In this paper, laser-induced graphene was successfully prepared on a thin and transparent polyimide film through the DLW process. Experiments have demonstrated that interdigital thin film capacitor prepared by [...] Read more.
Direct laser writing (DLW) is a convenient approach for fabricating graphene-based flexible electronic devices. In this paper, laser-induced graphene was successfully prepared on a thin and transparent polyimide film through the DLW process. Experiments have demonstrated that interdigital thin film capacitor prepared by the DLW method has a high specific capacitance of 8.11 mF/cm2 and volume capacitance density of 3.16 F/cm3 (0.05 mA/cm2) due to the doped fluoride in the laser-induced graphene. The capacitance is about 20 times larger than the super-capacitor based non-transparent polyimide film of the same thickness. Owing to its thin, flexible, higher electrochemical characteristics, the transparent polyimide film is promising for integrating and powering portable and wearable electronics. Full article
(This article belongs to the Section Nanofabrication and Nanomanufacturing)
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<p>Schematic illustration of fabrication process of (<b>a</b>–<b>d</b>) supercapacitor and (<b>e</b>) is physical image of supercapacitor.</p>
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<p>(<b>a</b>–<b>c</b>) The scanning electron microscope (SEM) images of the porous carbon materials prepared by DLW on transparent PI (DLWT)’s; (<b>a</b>–<b>b</b>) surface and (<b>c</b>) thickness cross-section; (<b>d</b>–<b>g</b>) the electron diffraction spectroscopy (EDS) mapping of C, N, O, F of DLWT surface; (<b>h</b>–<b>k</b>) the EDS mapping of C, N, O, F of thickness cross-section.</p>
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<p>(<b>a</b>) the Raman spectra of the porous carbon materials prepared by DLW on transparent PI and non-transparent PI (DLWT and DLWP) (Embedded graph is the Raman spectra of transparent polyimide film (PI)); (<b>b</b>) the X-ray photoelectron spectroscopy (XPS) spectra; (<b>c</b>) the high-resolution C 1s of DLWT; (<b>d</b>) the high-resolution F 1s of DLWT.</p>
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<p>The cyclic voltammetry (CV) curve of (<b>a</b>) DLWP and (<b>b</b>) DLWT with the scan rates of 5, 10, 20, 50, and 100 mV/s; (<b>c</b>) the CV curve comparison between DLWT and DLWP (scan rates is 100 mV/s); The galvanostatic charge/discharge (GCD) curve of (<b>d</b>) DLWP and (<b>e</b>) DLWT with the current density of 0.05, 0.1, 0.2, and 0.5 mA/cm<sup>2</sup>; (<b>f</b>) the GCD curve comparison of DLWT and DLWP (current density is 0.05 mA/cm<sup>2</sup>); specific capacitance (<b>g</b>) calculated from CV data (<b>h</b>) calculated from GCD data; (<b>i</b>) the Nyquist plots of DLWP and DLWT; (<b>j</b>) Ragone plot.</p>
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<p>(<b>a</b>) Normalized capacitance plot with 2500 charge/discharge cycles (Embedded graph is the initial CV curve after 500, 1000, 1500, 2000, and 2500 cycles number of DLWT with the scan rate of 0.1 V/s.); (<b>b</b>) DLWT CV curves of various bending radius under 0.1 V/s scan rate.</p>
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14 pages, 627 KiB  
Article
Exposure to Ultrafine Particles in the Ferroalloy Industry Using a Logbook Method
by Rikke Bramming Jørgensen, Ida Teresia Kero, Aleksander Blom, Esten Eide Grove and Kristin von Hirsch Svendsen
Nanomaterials 2020, 10(12), 2546; https://doi.org/10.3390/nano10122546 - 17 Dec 2020
Cited by 8 | Viewed by 3017
Abstract
Background: It is difficult to assess workers’ exposure to ultrafine particles (UFP) due to the lack of personal sampling equipment available for this particle fraction. The logbook method has been proposed as a general method for exposure assessment. This method measures the time [...] Read more.
Background: It is difficult to assess workers’ exposure to ultrafine particles (UFP) due to the lack of personal sampling equipment available for this particle fraction. The logbook method has been proposed as a general method for exposure assessment. This method measures the time and concentration components of the time-weighted average concentration separately and could be suitable for investigation of UFP exposure. Objectives: In this study, we have assessed workers’ exposure to UFP in a ferrosilicon plant. The main tasks of the furnace workers were identified, and the logbook method was used in combination with stationary measurements of UFP taken as close to the identified task areas as possible. In order to verify the results, respirable particles were collected using stationary sampling in close proximity to the UFP measuring instrument, and personal full-shift sampling of respirable particles was performed simultaneously. Thus, exposure to respirable particles determined using the logbook method could be compared to the results of standard measurement. Methods: The particle number concentration of ultrafine particles was determined using a NanoScan SMPS. Respirable particle concentration and exposure were determined using a sampling train consisting of a pump, filter, filter cassettes, and SKC Cyclone for the respirable fraction. Attendance times for workers at each work location were registered via thorough observations made by the research team. Results: The logbook method for exposure estimation based on stationary sampling equipment made it possible to calculate UFP exposure for workers operating the furnaces at a ferrosilicon plant. The mid-size furnace and the large furnace were evaluated separately. The workers operating the largest furnace were exposed to 1.47 × 104 particles/cm3, while workers operating the mid-size furnace were exposed to 2.06 × 104 particles/cm3, with a mean of 1.74 × 104 particles/cm3. Substantial contributions from the casting area, ladle transport corridor, and both tapping areas were made. Exposure to respirable particles was 2.04 mg/m3 (logbook); 2.26 mg/m3 (personal sampling) for workers operating the large-sized furnace, 3.24 mg/m3 (logbook); 2.44 mg/m3 (personal sampling) for workers operating the medium-sized furnace, and 2.57 mg/m3 (logbook); 2.53 mg/m3(personal sampling) on average of all tappers. The average ratio of these two methods’ results was 1.02, which indicates that the logbook method could be used as a substitute for personal sampling when it is not possible to perform personal sampling, at least within this industry. Conclusions: The logbook method is a useful supplement for exposure assessment of UFP, able to identify the most polluted areas of the workplace and the contribution of different work tasks to the total exposure of workers, enabling companies to take action to reduce exposure. Full article
(This article belongs to the Special Issue Safety and Biocompatibility of Metallic Nanoparticles)
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<p>Overview of processes in a typical smelter for ferrosilicon alloys. Reproduced from [<a href="#B6-nanomaterials-10-02546" class="html-bibr">6</a>] with permission from Springer Link 2017.</p>
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34 pages, 7567 KiB  
Article
The Kinetics and Stoichiometry of Metal Cation Reduction on Multi-Crystalline Silicon in a Dilute Hydrofluoric Acid Matrix
by Stefan Schönekerl and Jörg Acker
Nanomaterials 2020, 10(12), 2545; https://doi.org/10.3390/nano10122545 - 17 Dec 2020
Cited by 4 | Viewed by 2567
Abstract
In this study, the process of metal cation reduction on multi-crystalline silicon in a dilute hydrofluoric acid (HF) matrix is described using Ag(I), Cu(II), Au(III) and Pt(IV). The experimental basis utilized batch tests with various solutions of different metal cation and HF concentrations [...] Read more.
In this study, the process of metal cation reduction on multi-crystalline silicon in a dilute hydrofluoric acid (HF) matrix is described using Ag(I), Cu(II), Au(III) and Pt(IV). The experimental basis utilized batch tests with various solutions of different metal cation and HF concentrations and multi-crystalline silicon wafers. The metal deposition kinetics and the stoichiometry of metal deposition and silicon dissolution were calculated by means of consecutive sampling and analysis of the solutions. Several reaction mechanisms and reaction steps of the process were discussed by overlaying the results with theoretical considerations. It was deduced that the metal deposition was fastest if the holes formed during metal ion reduction could be transferred to the valence bands of the bulk and surface silicon with hydrogen termination. By contrast, the kinetics were lowest when the redox levels of the metal ion/metal half-cells were weak and the equilibrium potential of the H3O+/H2 half-cells was high. Further minima were identified at the thresholds where H3O+ reduction was inhibited, the valence transfer via valence band mechanism was limited by a Schottky barrier and the dissolution of oxidized silicon was restricted by the activity of the HF species F, HF2 and H2F3. The findings of the stoichiometric conditions provided further indications of the involvement of H3O+ and H2O as oxidizing agents in addition to metal ions, and the hydrogen of the surface silicon termination as a reducing agent in addition to the silicon. The H3O+ reduction is the predominant process in dilute metal ion solutions unless it is disabled due to the metal-dependent equilibrium potential of the H3O+/H2 half-cell and the energetic level of the valence bands of the silicon. As silicon is not oxidized up to the oxidation state +IV by the reduction of the metal ions and H3O+, water is suspected of acting as a secondary oxidant. The stoichiometric ratios increased up to a maximum with higher molalities of the metal ions, in the manner of a sigmoidal function. If, owing to the redox level of the metal half-cells and the energetic level of the valence band at the metal–silicon contact, the surface silicon can be oxidized, the hydrogen of the termination is the further reducing agent. Full article
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Figure 1

Figure 1
<p>Dissolved (<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au and (<b>d</b>) Pt species <span class="html-italic">b Me (diss., t = i)</span> and (<b>a</b>–<b>d</b>) Si species <span class="html-italic">b Si (diss., t = i)</span> at <span class="html-italic">t = i</span>; the period of the metal deposition phases 1 (<span class="html-italic">t</span> = 0 until <span class="html-italic">t</span><sub>1/2</sub>) and 2 (<span class="html-italic">t</span><sub>1/2</sub> until <span class="html-italic">t</span><sub>95%</sub>); the metal deposition rates <span class="html-italic">k</span><sub>1</sub> and <span class="html-italic">k</span><sub>2</sub>; the <span class="html-italic">t</span><sub>95%</sub>-weighted deposition rate <span class="html-italic">k</span><sub>95%</sub>; and the stoichiometric ratio of the change in molality of the dissolved metal ion <span class="html-italic">Δb Me</span> in relation to the change in molality of the dissolved silicon species Δ<span class="html-italic">b Si</span> in the period of <span class="html-italic">t</span> = 0 until <span class="html-italic">t</span><sub>95%</sub> (Δ<span class="html-italic">b Me</span>:Δ<span class="html-italic">b Si (diss., t<sub>95%</sub>)</span>).</p>
Full article ">Figure 2
<p>Metal deposition rates <span class="html-italic">k</span><sub>95%</sub> (<span class="html-italic">k</span><sub>95%,1</sub> and <span class="html-italic">k</span><sub>95%,2</sub>) of the (<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au and (<b>d</b>) Pt depositions in relation to the initial metal ion molality (<span class="html-italic">b Me (t = 0)</span>, Me = Ag, Cu, Au, Pt) or to the redox potential of the Me<sup>z+</sup>/Me half-cells <span class="html-italic">E (Me<sup>z+</sup>/Me)</span>. Red dots = examples from <a href="#nanomaterials-10-02545-f001" class="html-fig">Figure 1</a>, grey dots = findings with delayed silicon dissolution.</p>
Full article ">Figure 3
<p>Work functions <span class="html-italic">Φ</span> of the metals (<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au and (<b>d</b>) Pt and that of hydrogen-terminated Si in vacuum [<a href="#B65-nanomaterials-10-02545" class="html-bibr">65</a>,<a href="#B66-nanomaterials-10-02545" class="html-bibr">66</a>,<a href="#B67-nanomaterials-10-02545" class="html-bibr">67</a>,<a href="#B68-nanomaterials-10-02545" class="html-bibr">68</a>,<a href="#B69-nanomaterials-10-02545" class="html-bibr">69</a>,<a href="#B70-nanomaterials-10-02545" class="html-bibr">70</a>]; the difference in work functions Δ<span class="html-italic">E</span>; the Fermi energy level <span class="html-italic">E<sub>F</sub></span> and that of the valence and conduction band of hydrogen-terminated silicon [<a href="#B71-nanomaterials-10-02545" class="html-bibr">71</a>] (<span class="html-italic">E<sub>v</sub> (Si–H) or E<sub>c</sub> (Si–H)</span>) and of bulk silicon [<a href="#B72-nanomaterials-10-02545" class="html-bibr">72</a>,<a href="#B73-nanomaterials-10-02545" class="html-bibr">73</a>] (<span class="html-italic">E<sub>V</sub> (Si<sub>bulk</sub>)</span> or <span class="html-italic">E<sub>c</sub> (Si<sub>bulk</sub>)</span>); the energy levels of the valence bands at the metal–silicon contact (<span class="html-italic">E<sub>v</sub> (Si<sub>bulk</sub>/Me-Si</span>) or <span class="html-italic">E<sub>v</sub> (Si–H/Me-Si)</span>); the Schottky barrier <span class="html-italic">E<sub>sb</sub></span>; the redox levels of the Me<sup>z+</sup>/Me half-cells <span class="html-italic">E (Me<sup>z+</sup>/Me)</span>; and the equilibrium potentials of the 2H<sub>3</sub>O<sup>+</sup>/H<sub>2</sub> half-cells at the metal surface <span class="html-italic">Equation Pot. (2H<sub>3</sub>O<sup>+</sup>/H<sub>2</sub>)</span>.</p>
Full article ">Figure 4
<p><span class="html-italic">Left:</span> Sum of the initial activities of the anionic HF dissociation products F<sup>−</sup>, HF<sub>2</sub><sup>−</sup> and H<sub>2</sub>F<sub>3</sub><sup>−</sup> (<span class="html-italic">a (F<sup>−</sup> + HF<sub>2</sub><sup>−</sup> + H<sub>2</sub>F<sub>3</sub><sup>−</sup>) (t = 0)</span>) and molality of the dissolved silicon at <span class="html-italic">t</span><sub>95%</sub> (<span class="html-italic">b Si (diss., t<sub>95%</sub>)</span>) in relation to the initial metal ion molality: (<b>a</b>) <span class="html-italic">b Ag (diss., t = 0)</span> or (<b>b</b>) <span class="html-italic">b Cu (diss., t = 0)</span>. <span class="html-italic">Right</span>: Quotient of <span class="html-italic">a (F<sup>−</sup> + HF<sub>2</sub><sup>−</sup> + H<sub>2</sub>F<sub>3</sub><sup>−</sup>) (t = 0)</span> and <span class="html-italic">b Si (diss., t<sub>95%</sub>)</span> in relation to <span class="html-italic">b Ag (diss., t = 0)</span> or <span class="html-italic">b Cu (diss., t = 0)</span>. (Red dots = examples from <a href="#nanomaterials-10-02545-f001" class="html-fig">Figure 1</a>, grey dots = findings with delayed silicon dissolution).</p>
Full article ">Figure 5
<p>Stoichiometric ratios between the metal deposition Δ<span class="html-italic">b Me</span> ((<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au and (<b>d</b>) Pt) and silicon dissolution Δ<span class="html-italic">b Si</span> as a function of time <span class="html-italic">t</span> (Δ<span class="html-italic">b Me</span>:Δ<span class="html-italic">b Si (diss., t = i)</span>) based on the experiments of <a href="#nanomaterials-10-02545-f001" class="html-fig">Figure 1</a> with an indication of the <span class="html-italic">t</span><sub>95%</sub>-weighted stoichiometric ratios (red dots) and the corresponding minima and maxima (bars) denoted as (Δ<span class="html-italic">b Me</span>:Δ<span class="html-italic">b Si (diss., t<sub>95%</sub>)</span>).</p>
Full article ">Figure 6
<p>Stoichiometric ratios between the metal deposition Δ<span class="html-italic">b Me</span> ((<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au and (<b>d</b>) Pt) and silicon dissolution Δ<span class="html-italic">b Si</span> until <span class="html-italic">t</span><sub>95%</sub> (Δ<span class="html-italic">b Me</span>:Δ<span class="html-italic">b Si (diss., t<sub>95%</sub>)</span>), in relation to the initial metal ion molality (<span class="html-italic">b Me (diss., t = 0)</span>), are indicated as points for the <span class="html-italic">t</span><sub>95%</sub>-weighted values and as bars for the corresponding minima and maxima with delimitation by sigmoid functions <span class="html-italic">f</span><sub>1</sub>, <span class="html-italic">f</span><sub>2</sub> and <span class="html-italic">f<sub>3</sub></span> and classification of the underlying processes in <span class="html-italic">sections I</span>, <span class="html-italic">II</span>, <span class="html-italic">III</span> and <span class="html-italic">IV</span> (red dots = examples from <a href="#nanomaterials-10-02545-f001" class="html-fig">Figure 1</a>, grey dots = findings with limited silicon dissolution).</p>
Full article ">Figure 7
<p>Equilibrium potentials of the 2H<sub>3</sub>O<sup>+</sup>/H<sub>2</sub> half-cells at the (<b>a</b>) Ag, (<b>b</b>) Cu, (<b>c</b>) Au or (<b>d</b>) Pt surfaces (bright metal state/colloidal metal solution [<a href="#B76-nanomaterials-10-02545" class="html-bibr">76</a>]) in relation to the initial metal ion molalities (<span class="html-italic">b Me (diss., t = 0)</span>), the level of the Fermi energy <span class="html-italic">E<sub>F</sub></span> and levels of the valence bands of the bulk silicon (<span class="html-italic">E<sub>v</sub> (Si<sub>bulk</sub>/Me-Si</span>) and that of the hydrogen-terminated silicon (<span class="html-italic">E<sub>v</sub> (Si–H/Me-Si</span>)) at the metal–silicon contact. (Hollow symbols = oxonium ion reduction to molecular hydrogen possible, full symbols = no reaction).</p>
Full article ">Figure 8
<p>Molality of dissolved silicon in (<b>a</b>) gold deposition after <span class="html-italic">t</span> = 3600 s (<span class="html-italic">b Si (diss., t = 3600 s)</span>) and (<b>b</b>) platinum deposition after <span class="html-italic">t</span> = 14,400 s (<span class="html-italic">b Si (diss., t = 14,400 s</span>) in relation to the initial metal ion molality (<span class="html-italic">b Au (diss., t = 0)</span> and <span class="html-italic">b Pt (diss., t = 0)</span>, respectively) with and without the presence of para-chlorobenzoic acid (pCBA).</p>
Full article ">Figure 9
<p>Proposed scheme of the reaction of the ion pair H<sub>3</sub>O<sup>+</sup>∙F<sup>−</sup> with silicon.</p>
Full article ">Figure 10
<p>Reaction schemes of (<b>a</b>,<b>b</b>) silver, (<b>c</b>,<b>d</b>) copper, (<b>e</b>,<b>f</b>) gold and (<b>g</b>,<b>h</b>) platinum deposition on hydrogen-terminated silicon within <span class="html-italic">section III</span>.</p>
Full article ">Figure 11
<p>Reaction schemes of (<b>a</b>) silver, (<b>b</b>) copper, (<b>c</b>) gold and (<b>d</b>) platinum deposition on hydrogen-terminated silicon within <span class="html-italic">section IV</span>.</p>
Full article ">
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