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Nanomaterials, Volume 14, Issue 22 (November-2 2024) – 88 articles

Cover Story (view full-size image): This review highlights the unique potential of gold nanoparticles (AuNPs) for colorimetric nucleic acid detection, emphasizing their simplicity, rapidity, and cost-effectiveness while addressing key challenges like colloidal stability and oligonucleotide functionalization to enhance their sensitivity and specificity in complex biological fluids, paving the way for robust, low-cost biomedical sensors. View this paper
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13 pages, 5136 KiB  
Article
Thermal Decomposition of Core–Shell-Structured RDX@AlH3, HMX@AlH3, and CL-20@AlH3 Nanoparticles: Reactive Molecular Dynamics Simulations
by Zijian Sun, Lei Yang, Hui Li, Mengyun Mei, Lixin Ye, Jiake Fan and Weihua Zhu
Nanomaterials 2024, 14(22), 1859; https://doi.org/10.3390/nano14221859 - 20 Nov 2024
Viewed by 1021
Abstract
The reactive molecular dynamics method was employed to examine the thermal decomposition process of aluminized hydride (AlH3) containing explosive nanoparticles with a core–shell structure under high temperature. The core was composed of the explosives RDX, HMX, and CL-20, while the shell [...] Read more.
The reactive molecular dynamics method was employed to examine the thermal decomposition process of aluminized hydride (AlH3) containing explosive nanoparticles with a core–shell structure under high temperature. The core was composed of the explosives RDX, HMX, and CL-20, while the shell was composed of AlH3. It was demonstrated that the CL-20@AlH3 NPs decomposed at a faster rate than the other NPs, and elevated temperatures could accelerate the initial decomposition of the explosive molecules. The incorporation of aluminized hydride shells did not change the initial decomposition mechanism of the three explosives. The yields of the main products (NO, NO2, N2, H2O, H2, and CO2) were investigated. There was a large number of solid aluminized clusters produced during the decomposition, mainly AlmOn and AlmCn clusters, together with AlmNn clusters dispersed in the AlmOn clusters. Full article
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Graphical abstract
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<p>(<b>a</b>) Models of RDX/HMX/CL-20@AlH<sub>3</sub> NPs, (<b>b</b>) schematic diagram of aluminized hydride explosives with a core–shell structure. C, H, O, N, and Al atoms are represented by gray, white, red, blue, and pink balls, respectively.</p>
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<p>Snapshots of the morphology of RDX@AlH<sub>3</sub> NPs at 2400 K.</p>
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<p>Evolution of the number of the total species in the three AlH<sub>3</sub>-containing explosives with time at (<b>a</b>) 2100, (<b>b</b>) 2400, (<b>c</b>) 2700, and (<b>d</b>) 3000 K. Peak values (<b>e</b>) and number (<b>f</b>) of total species as a function of temperature.</p>
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<p>Time evolution of the products in the RDX@AlH<sub>3</sub> NPs at 2100, 2400, 2700, and 3000 K.</p>
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<p>Time evolution of the number of RDX, HMX, and CL-20 molecules at 2100, 2400, 2700, and 3000 K.</p>
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<p>Al<sub>m</sub>O<sub>n</sub> clusters in RDX @AlH<sub>3</sub> (<b>a</b>), HMX@AlH<sub>3</sub> (<b>b</b>), and CL-20@AlH<sub>3</sub> (<b>c</b>) NPs, and their basic unit (<b>d</b>).</p>
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<p>Al<sub>m</sub>C<sub>n</sub> clusters in the RDX @AlH<sub>3</sub> (<b>a</b>), HMX@AlH<sub>3</sub> (<b>b</b>), and CL-20@AlH<sub>3</sub> (<b>c</b>) NPs.</p>
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15 pages, 3703 KiB  
Article
Tuning Intermediate Band Solar Cell Efficiency: The Interplay of Electric Fields, Composition, Impurities, and Confinement
by Hassan Abboudi, Redouane En-nadir, Mohamed A. Basyooni-M. Kabatas, Ayoub El Baraka, Ilyass Ez-zejjari, Haddou El Ghazi and Ahmed Sali
Nanomaterials 2024, 14(22), 1858; https://doi.org/10.3390/nano14221858 - 20 Nov 2024
Viewed by 684
Abstract
In this study, we investigated the influence of structural parameters, including active region dimensions, electric field intensity, In-composition, impurity position, and potential profiles, on the energy levels, sub-gap transitions, and photovoltaic characteristics of a p-GaN/i-(In, Ga)N/GaN-n (p-QW-n) structure. The finite element method (FEM) [...] Read more.
In this study, we investigated the influence of structural parameters, including active region dimensions, electric field intensity, In-composition, impurity position, and potential profiles, on the energy levels, sub-gap transitions, and photovoltaic characteristics of a p-GaN/i-(In, Ga)N/GaN-n (p-QW-n) structure. The finite element method (FEM) has been used to solve numerically the Schrödinger equation. We found that particle and sub-gap energy levels are susceptible to well width, electric field, and impurity position. Particle energy decreases with increasing well size and electric field intensity, while impurity position affects energy based on proximity to the well center. Potential profile shapes, such as rectangular (RQW) and parabolic (PQW), also play a significant role, with PQW profiles providing stronger particle confinement. IB width increases with electric field intensity and saturates at higher In-content. Voc increases with field strength but decreases with In-content, and the parabolic profile yields higher efficiency than the rectangular one. Photovoltaic efficiency is improved with an appropriately oriented electric field and decreases with higher In-content and field intensity. These findings highlight the critical role of structural parameters in optimizing QW-IBSC performance. Full article
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Figure 1

Figure 1
<p>Schematic diagram of GaN/InGaN/GaN QW one-intermediate band integrated into the conventional solar cell under study considering the quantum well width <math display="inline"><semantics> <mrow> <mi>l</mi> </mrow> </semantics></math>, barriers height <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mo> </mo> <mi>V</mi> </mrow> <mrow> <mi>o</mi> </mrow> <mrow> <mi>e</mi> <mo>,</mo> <mi>h</mi> </mrow> </msubsup> </mrow> </semantics></math>, and built-in electric field <math display="inline"><semantics> <mrow> <mover accent="true"> <mrow> <mi>F</mi> </mrow> <mo>→</mo> </mover> </mrow> </semantics></math> (<math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>).</p>
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<p>The ground-state energy for electron (<b>left</b>) and heavy hole (<b>right</b>) versus the well and barrier widths for two potential profiles (PQW, RQW) with an on-center impurity and <math display="inline"><semantics> <mrow> <mi>T</mi> <mo>=</mo> <mn>300</mn> <mo> </mo> <mi mathvariant="normal">K</mi> <mo>,</mo> <mo> </mo> <mi>x</mi> <mo>=</mo> <mn>20</mn> <mo>%</mo> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mi>μ</mi> <mo>=</mo> <mn>0.5</mn> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>The energy of the electron (<b>left panel</b>) and hole (<b>right panel</b>) versus the well width in <math display="inline"><semantics> <mrow> <mi mathvariant="normal">G</mi> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">N</mi> </mrow> </semantics></math>/<math display="inline"><semantics> <mrow> <msub> <mrow> <mi mathvariant="normal">I</mi> <mi mathvariant="normal">n</mi> </mrow> <mrow> <mn>0.4</mn> </mrow> </msub> <msub> <mrow> <mi mathvariant="normal">G</mi> <mi mathvariant="normal">a</mi> </mrow> <mrow> <mn>0.6</mn> </mrow> </msub> </mrow> </semantics></math>N/<math display="inline"><semantics> <mrow> <mi mathvariant="normal">G</mi> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">N</mi> <mo> </mo> <mi mathvariant="normal">Q</mi> <mi mathvariant="normal">W</mi> <mo>−</mo> <mi mathvariant="normal">I</mi> <mi mathvariant="normal">B</mi> <mi mathvariant="normal">S</mi> <mi mathvariant="normal">C</mi> </mrow> </semantics></math> for two potential profiles. Two values of impurity’s positions and electric field are considered with <span class="html-italic">L</span> = 3<math display="inline"><semantics> <mrow> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <mo> </mo> <mi>x</mi> <mo>=</mo> <mn>40</mn> <mo>%</mo> </mrow> </semantics></math>, and T = 300 K for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>Transition energy (sub-gaps) versus the electric field (<b>left panel</b>) with <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>40</mn> <mo>%</mo> <mo> </mo> </mrow> </semantics></math> and compositions (<b>right panel</b>) with µ = 1 considering the effects of impurity position for two potential profiles (RQW and PQW) with <math display="inline"><semantics> <mrow> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> <mo> </mo> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>Intermediate band (IB width) as a function of the electric field (<b>left panel</b>) with <math display="inline"><semantics> <mrow> <mi>x</mi> <mo>=</mo> <mn>40</mn> <mo>%</mo> </mrow> </semantics></math> and compositions (<b>right panel</b>) with µ = 1 for two shapes (RQW and PQW). Two impurities (s positions are considered with <math display="inline"><semantics> <mrow> <mo> </mo> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mo>×</mo> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> <mo> </mo> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>The open circuit voltage variation versus the electric field intensity (<b>left</b>) and In-content (<b>right</b>) for two different impurity positions and two different profiles. <math display="inline"><semantics> <mrow> <mi mathvariant="normal">T</mi> <mo>=</mo> <mn>300</mn> <mo> </mo> <mi mathvariant="normal">K</mi> <mo>,</mo> <mo> </mo> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">d</mi> <mo> </mo> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>The variation of the short-circuit current density as a function of electric field strength (<b>left</b>) and In-content (<b>right</b>) for two different impurity positions considering the shape effect at room temperature. <math display="inline"><semantics> <mrow> <mi mathvariant="normal">T</mi> <mo>=</mo> <mn>300</mn> <mo> </mo> <mi mathvariant="normal">K</mi> <mo>,</mo> <mo> </mo> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">d</mi> <mo> </mo> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>Photovoltaic conversion efficiency versus the electric field (<b>left</b>) and In-content (<b>right</b>) at room temperature considering two different impurity positions and two types of potentials. <math display="inline"><semantics> <mrow> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>θ</mi> <mo>=</mo> <mn>0</mn> <mo>°</mo> </mrow> </semantics></math>.</p>
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<p>On-center impurity-related photovoltaic conversion efficiency versus the angle θ for different values of electric field strength and two different forms of potentials at room temperature. <math display="inline"><semantics> <mrow> <mi mathvariant="normal">x</mi> <mo>=</mo> <mn>0.5</mn> <mo>,</mo> <mo> </mo> <mi mathvariant="normal">a</mi> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">d</mi> <mo> </mo> <mi>L</mi> <mo>=</mo> <mn>3</mn> <mi>l</mi> <mo>=</mo> <mn>3</mn> <msup> <mrow> <mi>a</mi> </mrow> <mrow> <mi>*</mi> </mrow> </msup> </mrow> </semantics></math>.</p>
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16 pages, 4473 KiB  
Article
Nano-Silver-Loaded Activated Carbon Material Derived from Waste Rice Noodles: Adsorption and Antibacterial Performance
by Guanzhi Ding, Guangzhi Qin, Wanying Ying, Pengyu Wang, Yang Yang, Chuanyang Tang, Qing Liu, Minghui Li, Ke Huang and Shuoping Chen
Nanomaterials 2024, 14(22), 1857; https://doi.org/10.3390/nano14221857 - 20 Nov 2024
Viewed by 857
Abstract
This study demonstrates, for the first time, the conversion of waste rice noodles (WRN) into a cost-effective, nano-silver-loaded activated carbon (Ag/AC) material capable of efficient adsorption and antibacterial activity. The fabrication process began with the conversion of WRN into hydrothermal carbon (HTC) via [...] Read more.
This study demonstrates, for the first time, the conversion of waste rice noodles (WRN) into a cost-effective, nano-silver-loaded activated carbon (Ag/AC) material capable of efficient adsorption and antibacterial activity. The fabrication process began with the conversion of WRN into hydrothermal carbon (HTC) via a hydrothermal method. Subsequently, the HTC was combined with silver nitrate (AgNO3) and sodium hydroxide (NaOH), followed by activation through high-temperature calcination, during which AgNO3 was reduced to nano-Ag and loaded onto the HTC-derived AC, resulting in a composite material with both excellent adsorption properties and antibacterial activity. The experimental results indicated that the incorporation of nano-Ag significantly enhanced the specific surface area of the Ag/AC composite and altered its pore size distribution characteristics. Under optimized preparation conditions, the obtained Ag/AC material exhibited a specific surface area of 2025.96 m2/g and an average pore size of 2.14 nm, demonstrating effective adsorption capabilities for the heavy metal Cr(VI). Under conditions of pH 2 and room temperature (293 K), the maximum equilibrium adsorption capacity for Cr(VI) reached 97.07 mg/g. The adsorption behavior of the resulting Ag/AC fitted the Freundlich adsorption isotherm and followed a pseudo-second-order kinetic model. Furthermore, the Ag/AC composite exhibited remarkable inhibitory effects against common pathogenic bacteria such as E. coli and S. aureus, achieving antibacterial rates of 100% and 81%, respectively, after a contact time of 4 h. These findings confirm the feasibility of utilizing the HTC method to process WRN and produce novel AC-based functional materials. Full article
(This article belongs to the Section 2D and Carbon Nanomaterials)
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Figure 1

Figure 1
<p>Process flow diagram for simultaneous preparation of Ag/AC composite and photocatalytic composite (such as CQD/TiO<sub>2</sub> [<a href="#B27-nanomaterials-14-01857" class="html-bibr">27</a>], CQD/ZnO [<a href="#B28-nanomaterials-14-01857" class="html-bibr">28</a>,<a href="#B29-nanomaterials-14-01857" class="html-bibr">29</a>] and CQD/FeO<sub>x</sub> [<a href="#B30-nanomaterials-14-01857" class="html-bibr">30</a>]) using WRN as raw material.</p>
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<p>PXRD pattern of AC and Ag/AC composite.</p>
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<p>(<b>a</b>,<b>b</b>) The SEM image (<b>a</b>) and elemental mapping (<b>b</b>) of the Ag/AC composite based on WRN; (<b>c</b>,<b>d</b>) the TEM image (<b>c</b>) and HRTEM image (<b>d</b>) of the Ag/AC composite based on WRN.</p>
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<p>(<b>a</b>) IR spectra of AC and Ag/AC composite. (<b>b</b>) PZC value of AC and Ag/AC composite; (<b>c</b>–<b>f</b>) Full XPS (<b>c</b>), Ag 3d ((<b>d</b>), Ag/AC composite only), O 1s (<b>e</b>), and C 1s (<b>f</b>) high-resolution spectrum of AC and Ag/AC composite.</p>
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<p>(<b>a</b>,<b>b</b>) Nitrogen adsorption/desorption isotherms of Ag/AC composite (<b>a</b>) and AC without Ag loading (<b>b</b>). (<b>c</b>,<b>d</b>) Pore size distribution curves of Ag/AC composite (<b>c</b>) and AC without Ag loading (<b>d</b>).</p>
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<p>Adsorption isotherm of Ag/AC composite for Cr(VI): (<b>a</b>) experimental data, (<b>b</b>) Langmuir model, and (<b>c</b>) Freundlich model.</p>
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<p>(<b>a</b>) Langmuir adsorption isotherms of Cr (VI) on Ag/AC composite materials at different temperatures. (<b>b</b>) Relationship between ln k<sub>eq</sub> and 1/T.</p>
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<p>Dynamic adsorption equilibrium curve (<b>a</b>), fitted pseudo-first-order kinetic model (<b>b</b>) and pseudo-second-order kinetic model (<b>c</b>) of Ag/AC composite.</p>
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<p>(<b>a</b>,<b>b</b>): SEM image (<b>a</b>) and Cr(VI) elemental mapping (<b>b</b>) of Ag/AC composite after Cr(VI) adsorption; (<b>c</b>) PXRD patterns of Ag/AC composite before and after adsorption; (<b>d</b>) IR spectra of Ag/AC composite pre- and post-adsorption. Samples were treated in 150 mg·L<sup>−1</sup> Cr(VI) solution with 1 g·L<sup>−1</sup> adsorbent for 2 h.</p>
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<p>(<b>a</b>) Adsorption efficiency of Ag/AC composite for Cr(VI) in different water types. (<b>b</b>) Adsorption performance of Ag/AC composite for Cr(VI) after multiple adsorption–regeneration cycles.</p>
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<p>(<b>a</b>,<b>b</b>) Inhibition rates of AC and Ag/AC composite materials against <span class="html-italic">E. coli</span> (<b>a</b>) and <span class="html-italic">S. aureus</span> (<b>b</b>) for different times.</p>
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30 pages, 6585 KiB  
Review
Recent Progress on Advanced Flexible Lithium Battery Materials and Fabrication Process
by Mi Zhou, Daohong Han, Xiangming Cui, Jingzhao Wang, Xin Chen, Jianan Wang, Shiyi Sun and Wei Yan
Nanomaterials 2024, 14(22), 1856; https://doi.org/10.3390/nano14221856 - 20 Nov 2024
Viewed by 1259
Abstract
Flexible energy storage devices have attracted wide attention as a key technology restricting the vigorous development of wearable electronic products. However, the practical application of flexible batteries faces great challenges, including the lack of good mechanical toughness of battery component materials and excellent [...] Read more.
Flexible energy storage devices have attracted wide attention as a key technology restricting the vigorous development of wearable electronic products. However, the practical application of flexible batteries faces great challenges, including the lack of good mechanical toughness of battery component materials and excellent adhesion between components, resulting in battery performance degradation or failure when subjected to different types of deformation. It is imperative to develop flexible batteries that can withstand deformation under different conditions and maintain stable battery performance. This paper reviews the latest research progress of flexible lithium batteries, from the research and development of new flexible battery materials, advanced preparation processes, and typical flexible structure design. First, the types of key component materials and corresponding modification technologies for flexible batteries are emphasized, mainly including carbon-based materials with flexibility, lithium anode materials, and solid-state electrolyte materials. In addition, the application of typical flexible structural designs (buckling, spiral, and origami) in flexible batteries is clarified, such as 3D printing and electrospinning, as well as advanced fabrication techniques commonly used in flexible materials and battery components. Finally, the limitations and coping strategies in the practical application of flexible lithium batteries are discussed, which provides new ideas for future research. Full article
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Graphical abstract

Graphical abstract
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<p>Materials, process, and structure design of flexible batteries. Materials: C-base Collector. Reprinted with permission from Reference [<a href="#B4-nanomaterials-14-01856" class="html-bibr">4</a>]. Li-Wicking Hosts. Reprinted with permission from Reference [<a href="#B5-nanomaterials-14-01856" class="html-bibr">5</a>]. Solid-State Electrolytes (SSE). Reprinted with permission from Reference [<a href="#B6-nanomaterials-14-01856" class="html-bibr">6</a>]. Technics: 3DP-printing. Reprinted with permission from Reference [<a href="#B7-nanomaterials-14-01856" class="html-bibr">7</a>]. Electrostatic Spinning. Reprinted with permission from Reference [<a href="#B8-nanomaterials-14-01856" class="html-bibr">8</a>]. Electrodeposition. Reprinted with permission from Reference [<a href="#B9-nanomaterials-14-01856" class="html-bibr">9</a>]. Designs: Sectional Structure. Reprinted with permission from Reference [<a href="#B10-nanomaterials-14-01856" class="html-bibr">10</a>]. Spiral Structure. Reprinted with permission from Reference [<a href="#B11-nanomaterials-14-01856" class="html-bibr">11</a>]. Scale Structure. Reprinted with permission from Reference [<a href="#B12-nanomaterials-14-01856" class="html-bibr">12</a>].</p>
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<p>CNTs and graphene based flexible electrode materials. (<b>a</b>) The synthesis procedure of the MnO<sub>x</sub>/MWCNTs nanocomposites. Reprinted with permission from Reference [<a href="#B24-nanomaterials-14-01856" class="html-bibr">24</a>]. (<b>b</b>) The preparation procedure of flexible C@Fe<sub>2</sub>O<sub>3</sub>/SWCNT membrane. Reprinted with permission from Reference [<a href="#B29-nanomaterials-14-01856" class="html-bibr">29</a>]. (<b>c</b>) Stress-strain curves of Al-foil, CNT-P, and CF-CNT-P. Reprinted with permission from Reference [<a href="#B31-nanomaterials-14-01856" class="html-bibr">31</a>]. (<b>d</b>) Schematic of the synthesis process of TNGC material. Reprinted with permission from Reference [<a href="#B39-nanomaterials-14-01856" class="html-bibr">39</a>]. (<b>e</b>) Cycling performance of FVO/rGO and b-FVO materials (500 mAh g<sup>−1</sup>). Reprinted with permission from Reference [<a href="#B40-nanomaterials-14-01856" class="html-bibr">40</a>]. (<b>f</b>) Schematic illustration of the synthesis process of few-layer NbSe<sub>2</sub>@graphene by WBM. Reprinted with permission from Reference [<a href="#B41-nanomaterials-14-01856" class="html-bibr">41</a>]. (<b>g</b>) The cycling performance and corresponding coulombic efficiency of BDT/3DGraphene and BDT at 0.5 C. Reprinted with permission from Reference [<a href="#B44-nanomaterials-14-01856" class="html-bibr">44</a>].</p>
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<p>Other flexible carbon-based materials. (<b>a</b>) The synthesis procedure of Cu/Cu<sub>3</sub>P-N-CNFs current collector and (<b>b</b>) charge and discharge curves of Li-S battery assembled with Cu<sub>3</sub>P-N-CNFs anode. (<b>c</b>) The synthesis procedure of the MP<sub>x</sub>@NC composite materials and (<b>d</b>) rate performance and coulombic efficiency of Ni<sub>2</sub>P@NC//LFP full cell. Reprinted with permission from Reference [<a href="#B51-nanomaterials-14-01856" class="html-bibr">51</a>].</p>
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<p>Flexible lithium anode materials and their properties. (<b>a</b>) The preparation procedure of LMCY. Reprinted with permission from Reference [<a href="#B53-nanomaterials-14-01856" class="html-bibr">53</a>]. (<b>b</b>) The synthesis process of Li/AuCF anode. Reprinted with permission from Reference [<a href="#B56-nanomaterials-14-01856" class="html-bibr">56</a>]. (<b>c</b>) The cycling performance of lithium batteries at 1C of LFP|Cu@Li, LFP|MXene@Li and LFP|MXene@Au@Li. Reprinted with permission from Reference [<a href="#B57-nanomaterials-14-01856" class="html-bibr">57</a>]. (<b>d</b>) Schematic illustration of the process of lithium plating and stripping on MXene@CNF. Reprinted with permission from Reference [<a href="#B58-nanomaterials-14-01856" class="html-bibr">58</a>]. (<b>e</b>) Schematic illustration of lithium metal plating/stripping process on different substrates. (A) Exposed zinc nanosheets and (B) An interface layer with tent shaped nanocavities anchored by Zn-O-C bonds. Reprinted with permission from Reference [<a href="#B59-nanomaterials-14-01856" class="html-bibr">59</a>]. (<b>f</b>) Schematic illustration of LAGP/Li interface modified with rGO/ZnO (GZO). Reprinted with permission from Reference [<a href="#B61-nanomaterials-14-01856" class="html-bibr">61</a>].</p>
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<p>(<b>a</b>) Preparation of flowcharts of PEO-LiTFSI and PEO-PAN-LiTFSI. (<b>b</b>,<b>c</b>) SEM images of (<b>b</b>) the PAN fiber membrane and (<b>c</b>) PEO-PAN-LiTFSI. Reprinted with permission from Reference [<a href="#B66-nanomaterials-14-01856" class="html-bibr">66</a>]. (<b>d</b>) Diagram of wire-shaped cell. (<b>e</b>) (i)–(iv) Photographs of wire-shaped cells in different deformations. Reprinted with permission from Reference [<a href="#B67-nanomaterials-14-01856" class="html-bibr">67</a>]. (<b>f</b>) Schematic illustration for the synthesis of DN-Ionogel. (<b>g</b>) Schematic diagram of a flexible all-solid-state lithium battery and a hybrid interface composition during cycling. (<b>h</b>) The upholstery unit provides a display that powers the optical image of a large LED screen in a variety of conditions such as raw, bent, cut, and stamped. Reprinted with permission from Reference [<a href="#B69-nanomaterials-14-01856" class="html-bibr">69</a>].</p>
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<p>(<b>a</b>) Above: Flowchart of converting discarded clothing acrylic into a flexible wearable device. Bottom: Schematic diagram of the preparation of composite electrolytes from waste acrylic yarn. (<b>b</b>) Demonstration of the flexibility of pouch cells. (<b>c</b>) Flow diagram for the preparation of a solid electrolyte by incorporating f-NbS<sub>2</sub> nanosheets into a SPEEK matrix. (<b>d</b>) Capacitance retention and CE of FSSSC under different folding conditions. Reprinted with permission from Reference [<a href="#B6-nanomaterials-14-01856" class="html-bibr">6</a>].</p>
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<p>(<b>a</b>) Flow diagram of flexible electrode preparation by 3DP technology. (<b>b</b>) Cycling performance of the whole battery in both flat and curved states. Reprinted with permission from Reference [<a href="#B4-nanomaterials-14-01856" class="html-bibr">4</a>]. (<b>c</b>) Schematic illustration of the fabrication process of the 3D-printed TPU-based electrodes. Reprinted with permission from Reference [<a href="#B78-nanomaterials-14-01856" class="html-bibr">78</a>]. (<b>d</b>) Composition and morphological characteristics of retractable cell components, and advantages of retractable cells. Reprinted with permission from Reference [<a href="#B79-nanomaterials-14-01856" class="html-bibr">79</a>]. (<b>e</b>) Schematic diagram of the preparation of flexible Si@C NF using electrospinning technique. (<b>f</b>) Structural diagram of a flexible fiber paper electrode before carbonization. Reprinted with permission from Reference [<a href="#B8-nanomaterials-14-01856" class="html-bibr">8</a>].</p>
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<p>(<b>a</b>) Schematic chart of the fabrication for SiO<sub>x</sub>/E@CPPC. Reprinted with permission from Reference [<a href="#B86-nanomaterials-14-01856" class="html-bibr">86</a>]. (<b>b</b>) Schematic diagram of a stacked thin-film cell configuration. Reprinted with permission from Reference [<a href="#B89-nanomaterials-14-01856" class="html-bibr">89</a>]. (<b>c</b>) Schematic presentation of the simultaneous EPD process before and after application of electric field. Reprinted with permission from Reference [<a href="#B90-nanomaterials-14-01856" class="html-bibr">90</a>]. (<b>d</b>) Schematic diagram of the preparation process of the flexible cathode current collector. Reprinted with permission from Reference [<a href="#B91-nanomaterials-14-01856" class="html-bibr">91</a>]. (<b>e</b>) Overview diagram of electroplating each component of Li-based batteries. Reprinted with permission from Reference [<a href="#B92-nanomaterials-14-01856" class="html-bibr">92</a>]. (<b>f</b>) Schematic illustration of electrodeposition process.</p>
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<p>(<b>a</b>) Schematic diagram of a flexible structure battery for bone and joint bionics. Reprinted with permission from Reference [<a href="#B106-nanomaterials-14-01856" class="html-bibr">106</a>]. (<b>b</b>) Design concept diagram of a battery with flexible structure based on animal vertebrae biomimicry. Reprinted with permission from Reference [<a href="#B107-nanomaterials-14-01856" class="html-bibr">107</a>]. (<b>c</b>) Schematic diagram of the preparation of four CuO/Cu integrated folded electrodes. (<b>d</b>) Schematic diagram of a textile battery module. Reprinted with permission from Reference [<a href="#B114-nanomaterials-14-01856" class="html-bibr">114</a>]. (<b>e</b>) Fabrication process of the zigzag-like foldable battery. Reprinted with permission from Reference [<a href="#B115-nanomaterials-14-01856" class="html-bibr">115</a>]. (<b>f</b>) DNA helix structure and the helix-inspired battery design. Reprinted with permission from Reference [<a href="#B116-nanomaterials-14-01856" class="html-bibr">116</a>].</p>
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17 pages, 7201 KiB  
Article
Thermal Performance Analysis of a Nonlinear Couple Stress Ternary Hybrid Nanofluid in a Channel: A Fractal–Fractional Approach
by Saqib Murtaza, Nidhal Becheikh, Ata Ur Rahman, Aceng Sambas, Chemseddine Maatki, Lioua Kolsi and Zubair Ahmad
Nanomaterials 2024, 14(22), 1855; https://doi.org/10.3390/nano14221855 - 20 Nov 2024
Cited by 1 | Viewed by 723
Abstract
Nanofluids have improved thermophysical properties compared to conventional fluids, which makes them promising successors in fluid technology. The use of nanofluids enables optimal thermal efficiency to be achieved by introducing a minimal concentration of nanoparticles that are stably suspended in conventional fluids. The [...] Read more.
Nanofluids have improved thermophysical properties compared to conventional fluids, which makes them promising successors in fluid technology. The use of nanofluids enables optimal thermal efficiency to be achieved by introducing a minimal concentration of nanoparticles that are stably suspended in conventional fluids. The use of nanofluids in technology and industry is steadily increasing due to their effective implementation. The improved thermophysical properties of nanofluids have a significant impact on their effectiveness in convection phenomena. The technology is not yet complete at this point; binary and ternary nanofluids are currently being used to improve the performance of conventional fluids. Therefore, this work aims to theoretically investigate the ternary nanofluid flow of a couple stress fluid in a vertical channel. A homogeneous suspension of alumina, cuprous oxide, and titania nanoparticles is formed by dispersing trihybridized nanoparticles in a base fluid (water). The effects of pressure gradient and viscous dissipation are also considered in the analysis. The classical ternary nanofluid model with couple stress was generalized using the fractal–fractional derivative (FFD) operator. The Crank–Nicolson technique helped to discretize the generalized model, which was then solved using computer tools. To investigate the properties of the fluid flow and the distribution of thermal energy in the fluid, numerical methods were used to calculate the solution, which was then plotted as a function of various physical factors. The graphical results show that at a volume fraction of 0.04 (corresponding to 4% of the base fluid), the heat transfer rate of the ternary nanofluid flow increases significantly compared to the binary and unary nanofluid flows. Full article
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<p>Illustration of the model.</p>
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<p>Percentage of heat transfer enhancement of simple/unary, hybrid, and ternary hybrid nanofluids against volume fraction <math display="inline"><semantics> <mi>ϕ</mi> </semantics></math>.</p>
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<p>Classical, fractional, and fractal–fractional order temperature profiles when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">ϕ</span> = 0.02, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">M</span> = 2, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Temperature profile versus volume fraction <math display="inline"><semantics> <mi>ϕ</mi> </semantics></math> when <span class="html-italic">Ec</span> = 2, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">M</span> = 2, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Temperature profile versus Eckert number <span class="html-italic">Ec</span> when <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">M</span> = 2, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Classical, fractional, and fractal–fractional order velocity profile when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">ϕ</span> = 0.02, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">M</span> = 2, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Velocity profile versus couple stress parameter <span class="html-italic">η</span> when <span class="html-italic">E<sub>c</sub></span> = 2, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">t</span> = 3, <span class="html-italic">M</span> = 2, and <span class="html-italic">K</span> = 1.</p>
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<p>Velocity profile versus external pressure gradient <span class="html-italic">G</span> when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">t</span> = 3, <span class="html-italic">M</span> = 2, and <span class="html-italic">K</span> = 1.</p>
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<p>Velocity profile versus thermal Grashof number <span class="html-italic">Gr</span> when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">G</span> = 1, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">M</span> = 2, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Velocity profile versus magnetic parameter <span class="html-italic">M</span> when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, <span class="html-italic">t</span> = 3, and <span class="html-italic">K</span> = 1.</p>
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<p>Velocity profile versus porosity parameter <span class="html-italic">K</span> when <span class="html-italic">E<sub>C</sub></span> = 2, <span class="html-italic">G</span> = 1, <span class="html-italic">Gr</span> = 10, <span class="html-italic">η</span> = 1, <span class="html-italic">α</span> = <span class="html-italic">β</span> = 1, and <span class="html-italic">M</span> = 2.</p>
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56 pages, 5775 KiB  
Review
Gold Nanoparticles in Nanomedicine: Unique Properties and Therapeutic Potential
by Furkan Eker, Emir Akdaşçi, Hatice Duman, Mikhael Bechelany and Sercan Karav
Nanomaterials 2024, 14(22), 1854; https://doi.org/10.3390/nano14221854 - 20 Nov 2024
Cited by 2 | Viewed by 2604
Abstract
Gold nanoparticles (NPs) have demonstrated significance in several important fields, including drug delivery and anticancer research, due to their unique properties. Gold NPs possess significant optical characteristics that enhance their application in biosensor development for diagnosis, in photothermal and photodynamic therapies for anticancer [...] Read more.
Gold nanoparticles (NPs) have demonstrated significance in several important fields, including drug delivery and anticancer research, due to their unique properties. Gold NPs possess significant optical characteristics that enhance their application in biosensor development for diagnosis, in photothermal and photodynamic therapies for anticancer treatment, and in targeted drug delivery and bioimaging. The broad surface modification possibilities of gold NPs have been utilized in the delivery of various molecules, including nucleic acids, drugs, and proteins. Moreover, gold NPs possess strong localized surface plasmon resonance (LSPR) properties, facilitating their use in surface-enhanced Raman scattering for precise and efficient biomolecule detection. These optical properties are extensively utilized in anticancer research. Both photothermal and photodynamic therapies show significant results in anticancer treatments using gold NPs. Additionally, the properties of gold NPs demonstrate potential in other biological areas, particularly in antimicrobial activity. In addition to delivering antigens, peptides, and antibiotics to enhance antimicrobial activity, gold NPs can penetrate cell membranes and induce apoptosis through various intracellular mechanisms. Among other types of metal NPs, gold NPs show more tolerable toxicity capacity, supporting their application in wide-ranging areas. Gold NPs hold a special position in nanomaterial research, offering limited toxicity and unique properties. This review aims to address recently highlighted applications and the current status of gold NP research and to discuss their future in nanomedicine. Full article
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<p>Applications of gold NPs in various fields [<a href="#B3-nanomaterials-14-01854" class="html-bibr">3</a>,<a href="#B5-nanomaterials-14-01854" class="html-bibr">5</a>].</p>
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<p>Graph representing the published research papers that include “gold nanoparticles” in their title for the last 5 years, with a pie chart showing the distribution of applications based on the discussed sections [<a href="#B8-nanomaterials-14-01854" class="html-bibr">8</a>].</p>
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<p>General properties of gold nanoparticles [<a href="#B13-nanomaterials-14-01854" class="html-bibr">13</a>].</p>
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<p>Drug delivery application of gold NPs [<a href="#B29-nanomaterials-14-01854" class="html-bibr">29</a>].</p>
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<p>Nucleic acid delivery mechanism of gold NPs. Through endocytosis, functionalized gold NPs effectively transport nucleic acids into cells, and surface alterations improve targeting. The nucleic acids are released into the cytoplasm by endosomal escape mechanisms after internalization, providing opportunities for immunotherapy and gene therapy [<a href="#B61-nanomaterials-14-01854" class="html-bibr">61</a>].</p>
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<p>Representation of protein delivery mechanism of gold NPs. By altering their surfaces with ligands, polymers, or linkers, gold NPs may be made to bind particular proteins. This increases their circu-lation time and stops enzymatic breakdown. Through endocytosis, gold NPs enable cellular ab-sorption and release protein cargo inside cells. Therapeutic applications benefit from surface changes that improve targeting to certain tissues or cell types [<a href="#B75-nanomaterials-14-01854" class="html-bibr">75</a>].</p>
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<p>Gold NP-based photothermal and photodynamic therapy in anticancer application [<a href="#B52-nanomaterials-14-01854" class="html-bibr">52</a>,<a href="#B129-nanomaterials-14-01854" class="html-bibr">129</a>].</p>
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<p>Antibacterial activity of gold NPs by multiple mechanisms [<a href="#B209-nanomaterials-14-01854" class="html-bibr">209</a>].</p>
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<p>Potential toxicity mechanisms of gold NPs [<a href="#B257-nanomaterials-14-01854" class="html-bibr">257</a>,<a href="#B258-nanomaterials-14-01854" class="html-bibr">258</a>].</p>
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<p>Number of registered patents containing “Gold Nanoparticle” in their title in the last five years [<a href="#B277-nanomaterials-14-01854" class="html-bibr">277</a>].</p>
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14 pages, 2614 KiB  
Article
Synthesis and Characterization of Microcapsules as Fillers for Self-Healing Dental Composites
by Maria Amalia Tăut, Marioara Moldovan, Miuţa Filip, Ioan Petean, Codruţa Saroşi, Stanca Cuc, Adrian Catalin Taut, Ioan Ardelean, Viorica Lazăr and Sorin Claudiu Man
Nanomaterials 2024, 14(22), 1853; https://doi.org/10.3390/nano14221853 - 20 Nov 2024
Viewed by 760
Abstract
This article proposes the synthesis and characterization of (triethylene glycol dimethacrylate–N,N-dihydroxyethyl-p-toluidine) TEGDMA-DHEPT self-healing microcapsules for their inclusion in dental composite formulations. The obtaining method is the in situ emulsion polymerization of the (poly urea-formaldehyde) (PUF) coatings. The microcapsules were characterized by Fourier transform [...] Read more.
This article proposes the synthesis and characterization of (triethylene glycol dimethacrylate–N,N-dihydroxyethyl-p-toluidine) TEGDMA-DHEPT self-healing microcapsules for their inclusion in dental composite formulations. The obtaining method is the in situ emulsion polymerization of the (poly urea-formaldehyde) (PUF) coatings. The microcapsules were characterized by Fourier transform infrared spectroscopy (FTIR), scanning electron microscopy (SEM), atomic force microscopy (AFM), high-performance liquid chromatography (HPLC), and low-field nuclear magnetic resonance (NMR) techniques. The optimal formation of uniform microcapsules is achieved at a stirring speed of 800 rpm and centrifugation is no longer necessary. HPLC demonstrates that the microcapsules formed at 800 rpm show a better control of liquid release than the heterogeneous ones obtained at a lower stirring speed. The centrifuged samples have rounded shapes, with dimensions between 80 and 800 nm, while the non-centrifuged samples are more uniform, with a spherical shape and dimensions of approximately 800 nm. Full article
(This article belongs to the Section Biology and Medicines)
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<p>Obtaining microcapsules via in situ polymerization in an oil-in-water (O/W) emulsion.</p>
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<p>FTIR spectra of P2 and P3 samples.</p>
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<p>Microstructural investigation of nanocapsules after synthesis: SEM images of samples P1 (<b>a</b>) and P2 (<b>b</b>). Microstructure accompanied by ultrastructure as revealed by AFM: samples P1 (<b>a’</b>) and P2 (<b>b’</b>). Topographic 3D profile is presented below each AFM image.</p>
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<p>Nanocapsule diameter distribution for P1 and P2 samples.</p>
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<p>Microstructural investigation of nanocapsules after centrifugation: SEM images of samples P3 (<b>a</b>) and P4 (<b>b</b>). Microstructure accompanied by ultrastructure as revealed by AFM: samples P3 (<b>a’</b>) and P4 (<b>b’</b>). Topographic 3D profile is presented below each AFM image.</p>
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<p>HPLC chromatograms obtained for (<b>a</b>) TEGDMA standard, (<b>b</b>) sample P2 after 7 days and (<b>c</b>) sample P3 after 14 days.</p>
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<p>(<b>a</b>) The normalized FID signals recorded immediately after a 90-degree radiofrequency pulse. The steep decay corresponds to the solid-like component, and the slow decay to the liquid component. (<b>b</b>) The relaxation time distributions in the case of two samples (P2, P3) extracted via the CPMG technique. The largest peak corresponds to the liquid component inside the nanocapsules, and the smaller peaks may be associated with restricted molecular mobility as in solid-like components.</p>
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10 pages, 2327 KiB  
Article
Electric Field-Enhanced SERS Detection Using MoS2-Coated Patterned Si Substrate with Micro-Pyramid Pits
by Tsung-Shine Ko, Hsiang-Yu Hsieh, Chi Lee, Szu-Hung Chen, Wei-Chun Chen, Wei-Lin Wang, Yang-Wei Lin and Sean Wu
Nanomaterials 2024, 14(22), 1852; https://doi.org/10.3390/nano14221852 - 20 Nov 2024
Viewed by 766
Abstract
This study utilized semiconductor processing techniques to fabricate patterned silicon (Si) substrates with arrays of inverted pyramid-shaped micro-pits by etching. Molybdenum trioxide (MoO3) was then deposited on these patterned Si substrates using a thermal evaporation system, followed by two-stage sulfurization in [...] Read more.
This study utilized semiconductor processing techniques to fabricate patterned silicon (Si) substrates with arrays of inverted pyramid-shaped micro-pits by etching. Molybdenum trioxide (MoO3) was then deposited on these patterned Si substrates using a thermal evaporation system, followed by two-stage sulfurization in a high-temperature furnace to grow MoS2 thin films consisting of only a few atomic layers. During the dropwise titration of Rhodamine 6G (R6G) solution, a longitudinal electric field was applied using a Keithley 2400 (Cleveland, OH, USA) source meter. Raman mapping revealed that under a 100 mV condition, the analyte R6G molecules were effectively confined within the pits. Due to its two-dimensional structure, MoS2 provides a high surface area and supports a surface-enhanced Raman scattering (SERS) charge transfer mechanism. The SERS results demonstrated that the intensity in the pits of the few-layer MoS2/patterned Si SERS substrate was approximately 274 times greater compared to planar Si, with a limit of detection reaching 10−5 M. The experimental results confirm that this method effectively resolves the issue of random distribution of analyte molecules during droplet evaporation, thereby enhancing detection sensitivity and stability. Full article
(This article belongs to the Special Issue Nanoscale Photonics and Metamaterials)
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<p>(<b>a</b>) Lithography process flowchart. (<b>b</b>) Fabrication of the SERS substrate: Si substrate patterned with inverted pyramid pits, MoO<sub>3</sub> deposition, sulfurization to MoS<sub>2</sub>, and Cu electrode deposition. (<b>c</b>) SERS measurement setup: Cu electrodes are connected to a Keithley 2400 source meter to apply a longitudinal electric field for R6G localization.</p>
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<p>SEM images of (<b>a</b>) patterned Si, (<b>b</b>) MoO<sub>3</sub> deposited on patterned Si, and (<b>c</b>) MoS<sub>2</sub> formed on patterned Si. (<b>d</b>) Raman spectra of MoS<sub>2</sub> on patterned Si (blue) and planar Si (red), showing characteristic MoS<sub>2</sub> peaks.</p>
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<p>(<b>a</b>) SERS spectra for MoS<sub>2</sub>/patterned Si, patterned Si, and planar Si substrates with 10<sup>−3</sup> M R6G, showing enhanced signal for MoS<sub>2</sub>/patterned Si at 1362 cm<sup>−1</sup>. (<b>b</b>) SERS spectra of MoS<sub>2</sub>/patterned Si under different voltages, with optimal enhancement at 100 mV.</p>
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<p>Raman mapping images of R6G molecules on MoS<sub>2</sub>/patterned Si SERS substrate under applied voltages: (<b>a</b>) 0 mV, (<b>b</b>) 50 mV, (<b>c</b>) 100 mV, and (<b>d</b>) 150 mV, overlaid with corresponding OM images. The color scale represents signal intensity, ranging from blue (low) to red (high). Optimal SERS enhancement and uniform localization of R6G molecules within the pits are observed at 100 mV, whereas lower or higher voltages result in diminished signal intensity and less effective molecule aggregation.</p>
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<p>Raman mapping images of R6G on MoS<sub>2</sub>/patterned Si substrate at different concentrations: (<b>a</b>) 10<sup>−3</sup> M, (<b>b</b>) 10<sup>−4</sup> M, (<b>c</b>) 10<sup>−5</sup> M, and (<b>d</b>) 10<sup>−6</sup> M, overlaid with corresponding OM images. The signal intensity decreases as the concentration reduces, with strong and uniform signals observed at higher concentrations (10<sup>−3</sup> M), while the signals are significantly weaker at lower concentrations, indicating the detection limit around 10<sup>−5</sup> M.</p>
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17 pages, 2840 KiB  
Article
Green Synthesis of Al-ZnO Nanoparticles Using Cucumis maderaspatanus Plant Extracts: Analysis of Structural, Antioxidant, and Antibacterial Activities
by S. K. Johnsy Sugitha, R. Gladis Latha, Raja Venkatesan, Seong-Cheol Kim, Alexandre A. Vetcher and Mohammad Rashid Khan
Nanomaterials 2024, 14(22), 1851; https://doi.org/10.3390/nano14221851 - 20 Nov 2024
Viewed by 1020
Abstract
Nanoparticles derived from biological sources are currently garnering significant interest due to their diverse range of potential applications. The purpose of the study was to synthesize Al-doped nanoparticles of zinc oxide (ZnO) from leaf extracts of Cucumis maderaspatanus and assess their antioxidant and [...] Read more.
Nanoparticles derived from biological sources are currently garnering significant interest due to their diverse range of potential applications. The purpose of the study was to synthesize Al-doped nanoparticles of zinc oxide (ZnO) from leaf extracts of Cucumis maderaspatanus and assess their antioxidant and antimicrobial activity using some bacterial and fungal strains. These nanoparticles were analyzed using X-ray diffraction (XRD), ultraviolet–visible (UV-vis) spectroscopy, Fourier transform infrared spectroscopy (FTIR), scanning electron microscopy (SEM) with energy dispersive X-ray analysis (EDAX), transmission electron microscopy (TEM), and thermogravimetric analysis/differential thermal analysis (TG-DTA). The average crystalline size was determined to be 25 nm, as evidenced by the XRD analysis. In the UV-vis spectrum, the absorption band was observed around 351 nm. It was discovered that the Al-ZnO nanoparticles had a bandgap of 3.25 eV using the Tauc relation. Furthermore, by FTIR measurement, the presence of the OH group, C=C bending of the alkene group, and C=O stretching was confirmed. The SEM analysis revealed that the nanoparticles were distributed uniformly throughout the sample. The EDAX spectrum clearly confirmed the presence of Zn, Al, and O elements in the Al-ZnO nanoparticles. The TEM results also indicated that the green synthesized Al-ZnO nanoparticles displayed hexagonal shapes with an average size of 25 nm. The doping of aluminum may enhance the thermal stability of the ZnO by altering the crystal structure or phase composition. The observed changes in TG, DTA, and DTG curves reflect the impact of aluminum doping on the structural and thermal properties of ZnO nanoparticles. The antibacterial activity of the Al-ZnO nanoparticles using the agar diffusion method showed that the maximum zone of inhibition has been noticed against organisms of Gram-positive S. aureus compared with Gram-negative E. coli. Moreover, antifungal activity using the agar cup method showed that the maximum zone of inhibition was observed on Aspergilus flavus, followed by Candida albicans. Al-doping nanoparticles increases the number of charge carriers, which can enhance the generation of reactive oxygen species (ROS) under UV light exposure. These ROS are known to possess strong antimicrobial properties. Al-doping can improve the crystallinity of ZnO, resulting in a larger surface area that facilitates more interaction with microbial cells. The structural and biological characteristics of Al-ZnO nanoparticles might be responsible for the enhanced antibacterial activity exhibited in the antibacterial studies. Al-ZnO nanoparticles with Cucumis maderaspatanus leaf extract produced via the green synthesis methods have remarkable antioxidant activity by scavenging free radicals against DPPH radicals, according to these results. Full article
(This article belongs to the Special Issue Antimicrobial and Antioxidant Activity of Nanoparticles)
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<p>Schematic diagram of Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extract.</p>
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<p>Al-ZnO nanoparticles derived from <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts: (<b>A</b>) XRD pattern, (<b>B</b>) SEM, (<b>C</b>) EDAX.</p>
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<p>(<b>A</b>) and (<b>B</b>) TEM images of Al-ZnO nanoparticles, (<b>C</b>) SAED pattern of Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts.</p>
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<p>FTIR spectrum of the Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts.</p>
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<p>(<b>A</b>) UV spectrum, (<b>B</b>) Tauc plot of Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts.</p>
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<p>(<b>A</b>) Dynamic light scattering (DLS), and (<b>B</b>) zeta-potential measurement of Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts.</p>
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<p>TG/DTA curves of Al-ZnO nanoparticles using <span class="html-italic">Cucumis maderaspatanus</span> leaf extracts.</p>
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<p><span class="html-italic">Cucumis maderaspatanus</span> leaf extracts served to synthesize Al-ZnO, which exhibited antibacterial activity against (<b>A</b>) <span class="html-italic">S. aureus</span> and (<b>B</b>) <span class="html-italic">B. subtilitis</span>.</p>
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<p>The concentration verses antioxidant activity of % of inhibition Al-ZnO nanoparticles using the DPHH free radical assay method.</p>
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14 pages, 578 KiB  
Article
Effective Piecewise Mass Distributions for Optimal Energy Eigenvalues of a Particle in Low-Dimensional Heterojunctions
by Josep Batle, Orion Ciftja, Mahmoud Abdel-Aty, Mohamed Ahmed Hafez and Shawkat Alkhazaleh
Nanomaterials 2024, 14(22), 1850; https://doi.org/10.3390/nano14221850 - 20 Nov 2024
Viewed by 700
Abstract
Systems composed of several multi-layer compounds have been extremely useful in tailoring different quantum physical properties of nanomaterials. This is very much true when it comes to semiconductor materials and, in particular, to heterostructures and heterojunctions. The formalism of a position-dependent effective mass [...] Read more.
Systems composed of several multi-layer compounds have been extremely useful in tailoring different quantum physical properties of nanomaterials. This is very much true when it comes to semiconductor materials and, in particular, to heterostructures and heterojunctions. The formalism of a position-dependent effective mass has proved to be a very efficient tool in those cases where quantum wells emerge either in one or two dimensions. In this work, we use a variety of mathematical theorems, as well as numerical computations, to study different scenarios pertaining to choices of a specific piecewise constant effective mass for a particle that causes its energy eigenvalues to reach an extremum. These results are relevant when it comes to practical technological applications such as modifying the optical energy gap between the first excited state and the ground state energy of the system. At the end of our contribution, we also question the physical validity of some approximations for systems with particles that possess a position-dependent mass especially for those cases in which the mass distribution is divergent. Full article
(This article belongs to the Section Theory and Simulation of Nanostructures)
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<p>(Color online.) Different step-like mass distributions proposed for either 1D or 2D systems. (<b>a</b>–<b>d</b>) These are the four simplest stepwise functions used in this work. See text for details.</p>
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<p>(Color online.) Evolution of the ground state energy, <math display="inline"><semantics> <msub> <mi>E</mi> <mn>0</mn> </msub> </semantics></math>, as a function of parameter <math display="inline"><semantics> <msub> <mi>z</mi> <mn>0</mn> </msub> </semantics></math> for different values of <math display="inline"><semantics> <mrow> <mi>β</mi> <mo>/</mo> <mi>α</mi> </mrow> </semantics></math> (from top to bottom: <math display="inline"><semantics> <mrow> <mn>0.1</mn> <mo>,</mo> <mn>0.2</mn> <mo>,</mo> <mo>…</mo> <mo>,</mo> <mn>0.9</mn> </mrow> </semantics></math>). The corresponding results belong to the mass distribution in <a href="#nanomaterials-14-01850-f001" class="html-fig">Figure 1</a>a, which is not optimal. However, this structure can be of practical interest. The horizontal line corresponds to <math display="inline"><semantics> <mrow> <msub> <mi>E</mi> <mn>0</mn> </msub> <mo>=</mo> <msup> <mi>π</mi> <mn>2</mn> </msup> <mo>/</mo> <mn>8</mn> </mrow> </semantics></math> for <math display="inline"><semantics> <mrow> <mi>β</mi> <mo>/</mo> <mi>α</mi> <mo>=</mo> <mn>1</mn> </mrow> </semantics></math>. See text for details.</p>
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<p>(Color online.) (<b>a</b>) depicts maximum energies <math display="inline"><semantics> <msub> <mi>E</mi> <mn>0</mn> </msub> </semantics></math> as a function of <math display="inline"><semantics> <msub> <mi>z</mi> <mn>0</mn> </msub> </semantics></math> for several values of <math display="inline"><semantics> <mrow> <mi>β</mi> <mo>/</mo> <mi>α</mi> </mrow> </semantics></math>. (<b>b</b>) is equivalent to (<b>a</b>) but for minimum values <math display="inline"><semantics> <msub> <mi>E</mi> <mn>0</mn> </msub> </semantics></math>. (<b>c</b>) (with range doubled for the sake of clarity) and (<b>d</b>) display the results for the 2D mass distributions being maximum and minimum, respectively. The difference between various mass optimizers in 1D or 2D lies in the diverse concomitant boundary conditions. Horizontal lines correspond to concomitant 1D and 2D values of <math display="inline"><semantics> <msub> <mi>E</mi> <mn>0</mn> </msub> </semantics></math> for a constant mass, <math display="inline"><semantics> <mrow> <msub> <mi>m</mi> <mn>0</mn> </msub> <mo>=</mo> <mn>1</mn> </mrow> </semantics></math>. Colors have been added at the endpoints in (<b>c</b>) to highlight the almost linear behavior at the origin. See text for details.</p>
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17 pages, 5981 KiB  
Article
Free-Standing Carbon Nanofiber Films with Supported Cobalt Phosphide Nanoparticles as Cathodes for Hydrogen Evolution Reaction in a Microbial Electrolysis Cell
by Gerard Pérez-Pi, Jorge Luque-Rueda, Pau Bosch-Jimenez, Eduard Borràs Camps and Sandra Martínez-Crespiera
Nanomaterials 2024, 14(22), 1849; https://doi.org/10.3390/nano14221849 - 19 Nov 2024
Viewed by 1356
Abstract
High-performance and cost-efficient electrocatalysts and electrodes are needed to improve the hydrogen evolution reaction (HER) for the hydrogen (H2) generation in electrolysers, including microbial electrolysis cells (MECs). In this study, free-standing carbon nanofiber (CNF) films with supported cobalt phosphide nanoparticles have [...] Read more.
High-performance and cost-efficient electrocatalysts and electrodes are needed to improve the hydrogen evolution reaction (HER) for the hydrogen (H2) generation in electrolysers, including microbial electrolysis cells (MECs). In this study, free-standing carbon nanofiber (CNF) films with supported cobalt phosphide nanoparticles have been prepared by means of an up-scalable electrospinning process followed by a thermal treatment under controlled conditions. The produced cobalt phosphide-supported CNF films show to be nanoporous (pore volume up to 0.33 cm3 g−1) with a high surface area (up to 502 m2 g−1) and with a suitable catalyst mass loading (up to 0.49 mg cm−2). Values of overpotential less than 140 mV at 10 mA cm−2 have been reached for the HER in alkaline media (1 M KOH), which demonstrates a high activity. The high electrical conductivity together with the mechanical stability of the free-standing CNF films allowed their direct use as cathodes in a MEC reactor, resulting in an exceptionally low voltage operation (0.75 V) with a current density demand of 5.4 A m−2. This enabled the production of H2 with an energy consumption below 30 kWh kg−1 H2, which is highly efficient. Full article
(This article belongs to the Special Issue Hydrogen Production and Evolution Based on Nanocatalysts)
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<p>Pictures of the nanofiber films before (<b>left</b>) and after (<b>right</b>) the thermal treatment.</p>
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<p>XRD patterns of all CNFs samples including CoP, Co<sub>2</sub>P, and Co<sub>3</sub>O<sub>4</sub> diffraction patterns.</p>
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<p>XPS of Co<sub>2</sub>P@2h(165): (<b>a</b>) full spectrum, and (<b>b</b>) high resolution XPS spectra for C 1s, N 1s, P 2p, and Co 2p, respectively.</p>
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<p>Raman spectra of the samples Co<sub>2</sub>P@2h(165) and Co<sub>2</sub>Pox@2h(110).</p>
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<p>HRSEM and TEM images of the sample Co<sub>2</sub>P@2h(165) (<b>above</b>) and SAED pattern (<b>below</b>).</p>
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<p>LSV curves (<b>a</b>) and Tafel plots (<b>b</b>) for CNFs samples compared to the Pt/C used as reference.</p>
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<p>LSV performed at initial (straight lines) and after 1000 cycles (dotted lines) for Pt/C and Co<sub>2</sub>P@2h(140) electrodes.</p>
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<p>MEC reactors for assessing cathodes performances (<b>a</b>) and scheme of functioning (<b>b</b>).</p>
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<p>Polarization curves, j vs. V, (<b>a</b>) and electrode potentials followed up (<b>b</b>) for comparison of Co<sub>2</sub>P@2h(140) and Pt/C cathodes while operating in MEC reactors.</p>
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<p>HRSEM images of Co<sub>2</sub>P@2h(140), after being operated in the MEC reactor.</p>
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25 pages, 10477 KiB  
Article
Portable Homemade Magnetic Hyperthermia Apparatus: Preliminary Results
by Teresa Castelo-Grande, Paulo A. Augusto, Lobinho Gomes, Eduardo Calvo and Domingos Barbosa
Nanomaterials 2024, 14(22), 1848; https://doi.org/10.3390/nano14221848 - 19 Nov 2024
Viewed by 974
Abstract
This study aims to describe and evaluate the performance of a new device for magnetic hyperthermia that can produce an alternating magnetic field with adjustable frequency without the need to change capacitors from the resonant bank, as required by other commercial devices. This [...] Read more.
This study aims to describe and evaluate the performance of a new device for magnetic hyperthermia that can produce an alternating magnetic field with adjustable frequency without the need to change capacitors from the resonant bank, as required by other commercial devices. This innovation, among others, is based on using a capacitator bank that dynamically adjusts the frequency. To validate the novel system, a series of experiments were conducted using commercial magnetic nanoparticles (MNPs) demonstrating the device’s effectiveness and allowing us to identify new challenges associated with the design of more powerful devices. A computational model was also used to validate the device and to allow us to determine the best system configuration. The results obtained are consistent with those from other studies using the same MNPs but with magnetic hyperthermia commercial equipment, confirming the good performance of the developed device (e.g., consistent SAR values between 1.37 and 10.80 W/gMNP were obtained, and experiments reaching temperatures above 43 °C were also obtained). This equipment offers additional advantages, including being economical, user-friendly, and portable. Full article
(This article belongs to the Special Issue New Insights into the Therapeutic Efficacy of Nanomaterials)
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<p>Three-dimensional view of solenoid S5. (<b>a</b>) The copper coil contains interior water for cooling inside, while the surrounding domain contains air (<b>b</b>) computational mesh.</p>
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<p>Initial slope method (ISM) for calculating the specific absorption rate (SAR).</p>
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<p>Parallel LC resonant circuit.</p>
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<p>Image of the switch set that controls the capacitor bank.</p>
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<p>(<b>a</b>) Initial prototype of our system, (<b>b</b>) the system being currently applied, (<b>c</b>) a new and more powerful prototype system (resonant) that is being tested.</p>
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<p>Overview of the system (<b>a</b>) and photographs of the apparatus and of the system (<b>b</b>): A—power source; B—system; C—solenoid; D—cooling system; E—equipment for measuring temperature; F—computer for acquiring and registering the temperature; G and H—oscilloscope coupled with a probe for measuring the magnetic field and verifying the waveform passing through the coil [<a href="#B39-nanomaterials-14-01848" class="html-bibr">39</a>].</p>
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<p>Overview of the system (<b>a</b>) and photographs of the apparatus and of the system (<b>b</b>): A—power source; B—system; C—solenoid; D—cooling system; E—equipment for measuring temperature; F—computer for acquiring and registering the temperature; G and H—oscilloscope coupled with a probe for measuring the magnetic field and verifying the waveform passing through the coil [<a href="#B39-nanomaterials-14-01848" class="html-bibr">39</a>].</p>
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<p>Insulating system.</p>
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<p>Images of solenoids described in <a href="#nanomaterials-14-01848-t004" class="html-table">Table 4</a>.</p>
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<p>Profile of the magnetic field density (mT) of solenoid coil S5 for a driving voltage of 60 V and an operating frequency of 72 kHz. (<b>a</b>) Three-dimensional view, (<b>b</b>) two-dimensional view for the plane x = 0.</p>
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<p>Magnetic field density (mT) along the center of the simulated coils at various operating frequencies.</p>
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<p>The temperature variation of dstillated water samples was consistent across three experiments conducted on different days at a frequency of 69 kHz with solenoid S5.</p>
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<p>Heating curves for the Fluidmag<sub>ARA</sub> and Fluidmag<sub>UCA</sub> samples at a frequency 98 kHz using solenoid S5.</p>
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<p>Heating curves of Fluidmag<sub>D100nm</sub> (25 mg/mL) at 69 kHz using solenoid S5.</p>
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<p>Heating curves of Fluidmag<sub>D50nm</sub> (25 mg/mL) at 69 kHz using solenoid S5.</p>
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<p>Heating curves for the FluidMag<sub>D100nm</sub> sample at various frequencies using solenoid S5.</p>
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<p>Heating curves of various samples at a frequency of 138 kHz.</p>
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<p>Heating curves of FluidMag<sub>Dx100nn</sub> at different frequencies with a concentration of 12.5 mg<sub>MNP</sub>/mL using solenoid S6.</p>
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<p>Heating curves of FluidMag<sub>UCA</sub> at 72 kHz with a concentration of 12.5 mg<sub>MNP</sub>/mL using solenoid S8.</p>
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<p>Heating curves of FluidMag<sub>D100nm</sub> at different frequencies with a concentration of 12.5 mg<sub>MNP</sub>/mL using solenoid S8.</p>
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<p>Heating curves of FluidMag<sub>Dx50nm</sub> at different frequencies with a concentration of 25 mg<sub>MNP</sub>/mL using solenoid S8.</p>
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<p>Heating curves of FluidmagDX<sub>50nm</sub> samples with different concentrations (5 and 25 mg/m<sub>lMNP</sub>) at 132 kHz using solenoid S8.</p>
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<p>Heating and cooling curves of FluidMagDx50nm with the final configuration (S8).</p>
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28 pages, 1948 KiB  
Review
Nanomaterial-Enhanced Hybrid Disinfection: A Solution to Combat Multidrug-Resistant Bacteria and Antibiotic Resistance Genes in Wastewater
by Tapas Kumar Mandal
Nanomaterials 2024, 14(22), 1847; https://doi.org/10.3390/nano14221847 - 19 Nov 2024
Cited by 1 | Viewed by 1068
Abstract
This review explores the potential of nanomaterial-enhanced hybrid disinfection methods as effective strategies for addressing the growing challenge of multidrug-resistant (MDR) bacteria and antibiotic resistance genes (ARGs) in wastewater treatment. By integrating hybrid nanocomposites and nanomaterials, natural biocides such as terpenes, and ultrasonication, [...] Read more.
This review explores the potential of nanomaterial-enhanced hybrid disinfection methods as effective strategies for addressing the growing challenge of multidrug-resistant (MDR) bacteria and antibiotic resistance genes (ARGs) in wastewater treatment. By integrating hybrid nanocomposites and nanomaterials, natural biocides such as terpenes, and ultrasonication, this approach significantly enhances disinfection efficiency compared to conventional methods. The review highlights the mechanisms through which hybrid nanocomposites and nanomaterials generate reactive oxygen species (ROS) under blue LED irradiation, effectively disrupting MDR bacteria while improving the efficacy of natural biocides through synergistic interactions. Additionally, the review examines critical operational parameters—such as light intensity, catalyst dosage, and ultrasonication power—that optimize treatment outcomes and ensure the reusability of hybrid nanocomposites and other nanomaterials without significant loss of photocatalytic activity. Furthermore, this hybrid method shows promise in degrading ARGs, thereby addressing both microbial and genetic pollution. Overall, this review underscores the need for innovative wastewater treatment solutions that are efficient, sustainable, and scalable, contributing to the global fight against antimicrobial resistance. Full article
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<p>A schematic illustration depicting the limitations of conventional bacterial disinfection methods and the necessity for innovative disinfection strategies. Reprinted with permission from Ref. [<a href="#B23-nanomaterials-14-01847" class="html-bibr">23</a>] CC by 4.0.</p>
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<p>The diagram depicts the primary mechanisms involved in electro-oxidation, Electro-Fenton processes, ozone oxidation, and photocatalysis, all integrated with electrocoagulation for improved elimination of contaminants of emerging concern (CECs). Reprinted with permission from Ref. [<a href="#B44-nanomaterials-14-01847" class="html-bibr">44</a>] CC by 4.0.</p>
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<p>(<b>a</b>) Impact of radical scavengers on the photodegradation of methylene blue (MB) and (<b>b</b>) a schematic representation illustrating the photocatalytic mechanism of the NT/TiO<sub>2</sub> photocatalyst. Reprinted with permission from Ref. [<a href="#B102-nanomaterials-14-01847" class="html-bibr">102</a>], CC by 4.0.</p>
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<p>Mechanism of tetracycline degradation via photo-Fenton-like reaction. Reprinted with permission from Ref. [<a href="#B103-nanomaterials-14-01847" class="html-bibr">103</a>].</p>
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16 pages, 4681 KiB  
Article
M-Doped (M = Zn, Mn, Ni) Co-MOF-Derived Transition Metal Oxide Nanosheets on Carbon Fibers for Energy Storage Applications
by Andrés González-Banciella, David Martinez-Diaz, Adrián de Hita, María Sánchez and Alejandro Ureña
Nanomaterials 2024, 14(22), 1846; https://doi.org/10.3390/nano14221846 - 19 Nov 2024
Viewed by 956
Abstract
Carbon fiber, with its strong mechanical properties and electrical conductivity, is ideal as a fiber electrode in wearable or structural energy storage devices. However, its energy storage capacity is limited, and coatings like transition metal oxides (TMOs) enhance its electrochemical performance. Metal–organic frameworks [...] Read more.
Carbon fiber, with its strong mechanical properties and electrical conductivity, is ideal as a fiber electrode in wearable or structural energy storage devices. However, its energy storage capacity is limited, and coatings like transition metal oxides (TMOs) enhance its electrochemical performance. Metal–organic frameworks (MOFs) are commonly used to grow TMOs on carbon fibers, increasing the surface area for better energy storage. Despite this, TMOs have limited electrical conductivity, so ion exchange is often used to dope them with additional cations, improving both conductivity and energy storage capacity. This study compares different ion-exchange cations in ZIF-L-derived TMO coatings on carbon fiber. Testing both supercapacitor and Li-ion battery applications, Ni-doped samples showed superior results, attributed to their higher exchange ratio with cobalt. As a supercapacitor electrode, the Ni-doped material achieved 13.3 F/g at 50 mA/g—66% higher than undoped samples. For Li-ion battery anodes, it reached a specific capacity of 410.5 mAh/g at 25 mA/g, outperforming undoped samples by 21.4%. Full article
(This article belongs to the Special Issue Metal Organic Framework (MOF)-Based Micro/Nanoscale Materials)
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<p>SEM images of ZIF-L coating on carbon fiber fabric at (<b>a</b>) lower magnification and (<b>b</b>) higher magnification, (<b>c</b>) undoped TMO sample, (<b>d</b>) Zn-doped TMO sample, (<b>e</b>) Mn-doped TMO sample, and (<b>f</b>) Ni-doped TMO sample.</p>
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<p>(<b>a</b>) XPS surveys. (<b>b</b>) XPS Co 2p core level of the undoped sample. (<b>c</b>) XPS Zn 2p core level of Zn-doped sample. (<b>d</b>) XPS Mn 2p core level of Mn-doped sample. (<b>e</b>) XPS Ni 2p core level of Ni-doped sample. (<b>f</b>) The atomic percentage of each cation in each sample. (<b>g</b>) XRD spectra of TMO powder samples.</p>
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<p>TEM images of undoped TMO samples at (<b>a</b>) lower and (<b>b</b>) higher magnification.</p>
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<p>(<b>a</b>) CV curves at a scan rate of 20 mV/s. (<b>b</b>) Specific capacitance values are calculated from CV at 20 mV/s. (<b>c</b>) GCD test discharges at 50 mA/g. (<b>d</b>) Specific capacitance calculated from GCD tests at different current densities.</p>
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<p>(<b>a</b>) CV curve of Ni-doped sample at different scan rates and (<b>b</b>) calculated <span class="html-italic">b</span> value in the inset. (<b>c</b>) Diffusion and capacitive-controlled processes contribute to different scan rates for Ni-doped samples. (<b>d</b>) Specific capacitance and coulombic efficiency of Ni-doped sample after 5000 GCD cycles at 150 mA/g.</p>
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<p>(<b>a</b>) Normalized third-cycle CV of the samples. (<b>b</b>) GCD curves at 25 mA/g of the samples. (<b>c</b>) GCD calculated capacities at different current densities. (<b>d</b>) Nyquist plots of the samples.</p>
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<p>(<b>a</b>) Ni-doped sample CV at different scan rates and calculated b value in the inset. (<b>b</b>) Percentage of each contribution at different scan rates in the Ni-doped sample. (<b>c</b>) Specific capacity of Ni-doped sample after 100 GCD cycles at 100 mA/g. (<b>d</b>) Nyquist plot of Ni-doped sample after several number of cycles.</p>
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5 pages, 198 KiB  
Editorial
Micro- and Nanostructured Biomaterials for Biomedical Applications and Regenerative Medicine
by Michele Bianchi and Gianluca Carnevale
Nanomaterials 2024, 14(22), 1845; https://doi.org/10.3390/nano14221845 - 18 Nov 2024
Viewed by 1068
Abstract
Over the past two decades, research on innovative micro- and nano-biomaterials has seen a significant surge in the bioengineering, biomedicine, and regenerative medicine fields [...] Full article
13 pages, 3286 KiB  
Article
Improving the NO2 Gas Sensing Performances at Room Temperature Based on TiO2 NTs/rGO Heterojunction Nanocomposites
by Yan Ling, Yunjiang Yu, Canxin Tian and Changwei Zou
Nanomaterials 2024, 14(22), 1844; https://doi.org/10.3390/nano14221844 - 18 Nov 2024
Cited by 1 | Viewed by 887
Abstract
The development of energy-efficient, sensitive, and reliable gas sensors for monitoring NO2 concentrations has garnered considerable attention in recent years. In this manuscript, TiO2 nanotube arrays/reduced graphene oxide nanocomposites with varying rGO contents (TiO2 NTs/rGO) were synthesized via a two-step [...] Read more.
The development of energy-efficient, sensitive, and reliable gas sensors for monitoring NO2 concentrations has garnered considerable attention in recent years. In this manuscript, TiO2 nanotube arrays/reduced graphene oxide nanocomposites with varying rGO contents (TiO2 NTs/rGO) were synthesized via a two-step method for room temperature NO2 gas detection. From SEM and TEM images, it is evident that the rGO sheets not only partially surround the TiO2 nanotubes but also establish interconnection bridges between adjacent nanotubes, which is anticipated to enhance electron–hole separation by facilitating electron transfer. The optimized TiO2 NTs/rGO sensor demonstrated a sensitive response of 19.1 to 1 ppm of NO2, a 5.26-fold improvement over the undoped TiO2 sensor. Additionally, rGO doping significantly enhanced the sensor’s response/recovery times, reducing them from 24 s/42 s to 18 s/33 s with just 1 wt.% rGO. These enhancements are attributed to the increased specific surface area, higher concentration of chemisorbed oxygen species, and the formation of p-n heterojunctions between TiO2 and rGO within the nanocomposites. This study provides valuable insights for the development of TiO2/graphene-based gas sensors for detecting oxidizing gases at room temperature. Full article
(This article belongs to the Special Issue Design and Applications of Heterogeneous Nanostructured Materials)
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<p>Schematic of synthesis process (<b>a</b>) and photograph of NO<sub>2</sub> detection testing system (<b>b</b>).</p>
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<p>XRD patterns of TiO<sub>2</sub> NTs/rGO nanocomposites grown with different rGO contents.</p>
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<p>SEM images of TiO<sub>2</sub> NTs/rGO nanocomposites with rGO contents of 0 wt.% (<b>a</b>), 0.5 wt.% (<b>b</b>), 1 wt.% (<b>c</b>), and 3 wt.% (<b>d</b>), respectively. Inset of <a href="#nanomaterials-14-01844-f003" class="html-fig">Figure 3</a>d shows the EDX spectrum of TiO<sub>2</sub> NTs/rGO nanocomposites with rGO contents of 3 wt.%. The red circles in <a href="#nanomaterials-14-01844-f003" class="html-fig">Figure 3</a>d illustrate the structure of rGO surrounding the TiO<sub>2</sub> nanotubes.</p>
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<p>TEM (<b>a</b>,<b>b</b>) and high-resolution TEM (<b>c</b>,<b>d</b>) images of TiO<sub>2</sub> nanotubes (<b>a</b>,<b>c</b>) and TiO<sub>2</sub> NTs/rGO nanocomposites (<b>b</b>,<b>d</b>) with rGO contents of 1 wt.%.</p>
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<p>Raman spectra of TiO2 NTs/rGO nanocomposites with different rGO contents.</p>
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<p>XPS spectra of TiO<sub>2</sub> NTs/rGO nanocomposite with rGO contents of 1 wt.%. (<b>a</b>) Full scan. (<b>b</b>) Ti 2p. (<b>c</b>) C 1s. (<b>d</b>) O 1s.</p>
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<p>The response value of the sensor based on TiO<sub>2</sub> NTs/rGO composites vs. NO<sub>2</sub> concentration at room temperature.</p>
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<p>The dynamic response transients of the sensor based on TiO<sub>2</sub> NTs/rGO nanocomposites to 20 ppm NO<sub>2</sub> at room temperature.</p>
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<p>Response of the sensor based on TiO<sub>2</sub> NTs/rGO nanocomposites to 50 ppm of C<sub>2</sub>H<sub>5</sub>OH, CH<sub>3</sub>OH, H<sub>2</sub>, NH<sub>3</sub>, H<sub>2</sub>S, and NO<sub>2</sub> at room temperature.</p>
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<p>Long-term stability of the sensor based on TiO<sub>2</sub> NTs and TiO<sub>2</sub> NTs/rGO nanocomposites to 1 ppm of NO<sub>2</sub> at room temperature.</p>
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<p>I-V curves of the sensor based on TiO<sub>2</sub> NTs/rGO nanocomposites with different rGO contents.</p>
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<p>Energy band diagrams for TiO<sub>2</sub> NTs, rGO and TiO<sub>2</sub> NTs/rGO heterostructure, where E<sub>VB</sub>, E<sub>F</sub>, E<sub>CB</sub>, E<sub>vac</sub> represent valence band, Fermi level, conduction band, and vacuum level, respectively. (<b>a</b>) The energy band diagrams for TiO<sub>2</sub> nanotubes, rGO, and their corresponding TiO<sub>2</sub> NTs/rGO nanocomposites. (<b>b</b>) Schematic illustration of electron transfer and sensing mechanism of TiO<sub>2</sub> NTs/rGO nanocomposites.</p>
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12 pages, 5364 KiB  
Article
Controlled Formation of Silicon-Vacancy Centers in High-Pressure Nanodiamonds Produced from an “Adamantane + Detonation Nanodiamond” Mixture
by Dmitrii G. Pasternak, Rustem H. Bagramov, Alexey M. Romshin, Igor P. Zibrov, Vladimir P. Filonenko and Igor I. Vlasov
Nanomaterials 2024, 14(22), 1843; https://doi.org/10.3390/nano14221843 - 18 Nov 2024
Viewed by 916
Abstract
Despite progress in the high-pressure synthesis of nanodiamonds from hydrocarbons, the problem of controlled formation of fluorescent impurity centers in them still remains unresolved. In our work, we explore the potential of a new precursor composition, a mixture of adamantane with detonation nanodiamond, [...] Read more.
Despite progress in the high-pressure synthesis of nanodiamonds from hydrocarbons, the problem of controlled formation of fluorescent impurity centers in them still remains unresolved. In our work, we explore the potential of a new precursor composition, a mixture of adamantane with detonation nanodiamond, both in the synthesis of nanodiamonds and in the controlled formation of negatively charged silicon-vacancy centers in such nanodiamonds. Using different adamantane/detonation nanodiamond weight ratios, a series of samples was synthesized at a pressure of 7.5 GPa in the temperature range of 1200–1500 °C. It was found that temperature around 1350 °C, is optimal for the high-yield synthesis of nanodiamonds <50 nm in size. For the first time, controlled formation of negatively charged silicon-vacancy centers in such small nanodiamonds was demonstrated by varying the atomic ratios of silicon/carbon in the precursor in the range of 0.01–1%. Full article
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<p>(<b>a</b>) XRD patterns of four different HPHT samples synthesized at 1250 °C from adamantane/DND mixture in the following weight proportions: 0/1, 1/1, 10/1 and 100/1. For convenience of comparative analysis, the diffraction patterns are normalized to the intensity of the (220) diamond diffraction peak, and the background associated with the scattering of X-rays on the substrate is subtracted from them. D—diamond, G—graphite. (<b>b</b>) Zoomed part of XRD pattern around (220) diamond diffraction peak.</p>
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<p>(<b>a</b>) SEM images of samples synthesized at 1250 °C from adamantane/DND mixture in weight proportion 10/1 (<b>a</b>) and 100/1 (<b>b</b>).</p>
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<p>(<b>a</b>) Wide-angle XRD patterns of “1/1” (black) and “25/1” (red) samples synthesized at 1350 and 1450 °C. (<b>b</b>) Approximation of (220) diamond diffraction peaks by Lorentz profiles for samples “1/1” and “25/1” synthesized at 1350 °C. The peak shape is most accurately fitted by the superposition of three profiles. The arrows indicate the average sizes of diamond nanoparticles estimated for each profile.</p>
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<p>SEM, TEM images and Raman spectrum of the sample “25/1” synthesized at 1350 °C. (<b>a</b>) SEM image of diamond nanoparticles dispersed on a substrate from alcohol suspension. (<b>b</b>) TEM image of the ND agglomerate prepared by drying a drop of the suspension on a grid. The characteristic sizes of diamond crystallites are less than 10 nm in the marked area A, and 20–50 nm in the area B. (<b>c</b>) Typical Raman spectrum of the sample. The diamond peak (orange dotted line) is shifted to the position of 1332.1 cm<sup>−</sup><sup>1</sup> and broadened up to 5.7 cm<sup>−1</sup> relative to the diamond peak (black line) recorded for the natural bulk IIa diamond.</p>
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<p>PL spectra of the samples synthesized at 1350 °C from adamantane/DND/tetrakis mixture at adamantane/DND weight proportions 25/1 (red) and 1/1 (black), and Si/C atomic ratio 1%. The spectra are normalized to the intensity of the diamond Raman (DR) line. Zero-phonon line of SiV<sup>−</sup> center and DR line are observed at 738.5 nm and 504.8 nm, respectively. “Palisade” of narrow lines observed throughout the range 500–800 nm is typical for N-doped H-terminated NDs [<a href="#B43-nanomaterials-14-01843" class="html-bibr">43</a>].</p>
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<p>(<b>a</b>) PL spectra of the sample “25/1” synthesized at 1350 °C from adamantane/DND/tetrakis mixture with atomic ratio Si/C varying from 0% to 1%. The spectra are normalized to the intensity of the diamond Raman (DR) line. (<b>b</b>) The dependence of the integrated fluorescence intensity SiV<sup>−</sup> normalized to the DR line (I<sup>int</sup><sub>SiV/DR</sub>) on the atomic ratio Si/C in the precursor. The statistical error in determining I<sup>int</sup><sub>SiV/DR</sub>/DR was calculated based on averaging ten PL spectra for each of the five samples.</p>
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<p>Raman spectrum of the sample synthesized at 1350 °C from chloradamantane/tetrakis mixture with atomic ratio Si/C = 1/1000. Only the lines of DR (504.8 nm) and the stretching vibrations of surface CHx groups (near 550 nm) are observed in the spectrum.</p>
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<p>XRD pattern of three samples: initial (black), treated at 7.5 GPa pressure and temperatures of 1250 °C (orange) and 1450 °C (red). Only diffraction peaks of diamond are observed in all three samples. The estimation of the crystallite sizes according to the Scherrer formula indicates that the average size of diamond crystallites increases from 4–5 nm (initial) to 7 nm (1450 °C). Note that amorphous carbon, which dominates in the Raman spectra (see below), is not detected by the XRD.</p>
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<p>(<b>a</b>) The typical Raman spectrum of the untreated DND consists of an asymmetric diamond peak (DR) at 1328.5 cm<sup>−1</sup> and a band at 1630 cm<sup>−1</sup> that overlap with the initial fragment of broadband (500–700 nm) fluorescence background [<a href="#B37-nanomaterials-14-01843" class="html-bibr">37</a>]. (<b>b</b>) Typical Raman spectrum of DND treated at 1450 °C is characterized by a broad band of amorphous carbon (1300–1600 cm<sup>−1</sup>), which dominates the spectrum [<a href="#B49-nanomaterials-14-01843" class="html-bibr">49</a>]; a diamond (DR) peak is barely distinguished against the fluorescence background. Similar Raman spectra were observed for DND treated at 1250 °C.</p>
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13 pages, 2793 KiB  
Article
Nature of the Pits on the Lattice-Matched InAlAs Layer Surface Grown on the (001) InP Substrate
by Dmitrii V. Gulyaev, Demid S. Abramkin, Dmitriy V. Dmitriev, Alexander I. Toropov, Eugeniy A. Kolosovsky, Sergey A. Ponomarev, Nina N. Kurus, Ilya A. Milekhin and Konstantin S. Zhuravlev
Nanomaterials 2024, 14(22), 1842; https://doi.org/10.3390/nano14221842 - 18 Nov 2024
Viewed by 772
Abstract
The structural properties of lattice-matched InAlAs/InP layers grown by molecular beam epitaxy have been studied using atomic force microscopy, scanning electron microscopy and micro-photoluminescence spectroscopy. The formation of the surface pits with lateral sizes in the micron range and a depth of about [...] Read more.
The structural properties of lattice-matched InAlAs/InP layers grown by molecular beam epitaxy have been studied using atomic force microscopy, scanning electron microscopy and micro-photoluminescence spectroscopy. The formation of the surface pits with lateral sizes in the micron range and a depth of about 2 ÷ 10 nm has been detected. The InP substrate annealing temperature and value of InAlAs alloy composition deviation from the lattice-matched InxAl1−xAs/InP case (x = 0.52) control the density of pits ranging from 5 × 105 cm−2 ÷ 108 cm−2. The pit sizes are controlled by the InAlAs layer thickness and growth temperature. The correlation between the surface pits and threading dislocations has been detected. Moreover, the InAlAs surface is characterized by composition inhomogeneity with a magnitude of 0.7% with the cluster lateral sizes and density close to these parameters for surface pits. The experimental data allow us to suggest a model where the formation of surface pits and composition clusters is caused by the influence of a local strain field in the threading dislocation core vicinity on In adatoms incorporating kinetic. Full article
(This article belongs to the Section Nanophotonics Materials and Devices)
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<p>Scheme of structures with In<sub>x</sub>Al<sub>1−x</sub>As layer with thickness <span class="html-italic">D</span> grown at <span class="html-italic">T</span><sub>S</sub>. The preparation of the InP substrate was performed at <span class="html-italic">T</span><sub>A</sub>. The InAsP layer, formed during the substrate preparation, is marked as «InAsP».</p>
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<p>AFM images of 1 μm thick InAlAs layers lattice-matched with the substrate. <span class="html-italic">T</span><sub>A</sub> = 485 °C and <span class="html-italic">T</span><sub>S</sub> = 485 °C for (<b>A</b>) and <span class="html-italic">T</span><sub>A</sub> = 535 °C, <span class="html-italic">T</span><sub>S</sub> = 525 °C for (<b>B</b>). Total layer thickness is 1000 nm for both structures. Relief profiles are presented in the insets.</p>
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<p>(<b>a</b>) The dependence of the pit density on the substrate annealing temperature for the lattice-matched layer (<span class="html-italic">x</span> = 0.52, black dots) and on the layer composition deviation from the lattice-matched value (red dots). (<b>b</b>) The dependence of the lateral size of the pits on the InAlAs layer thickness for <span class="html-italic">x</span> = 0.52 (black dots) and <span class="html-italic">x</span> = 0.51 (red dots). (<b>c</b>) The dependence of the depth of the pits on the thickness of the InAlAs layer with <span class="html-italic">x</span> = 0.52 grown at the temperature of 505 °C. (<b>d</b>) The dependence of the depth of the pits on the growth temperature for the InAlAs layer with <span class="html-italic">x</span> = 0.52 grown at the total layer thickness of 1 μm.</p>
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<p>The SEM cross-sectional image of the heterostructure grown at <span class="html-italic">T</span><sub>A</sub> = 535 °C, <span class="html-italic">T</span><sub>S</sub> = 525 °C and <span class="html-italic">D</span> = 1000 nm, with the alloy composition deviation of 0.5%. The vertical arrows at the top panel point to the surface pits. The bottom panel shows the same area of the SEM image but with the dislocations indicated by thin white lines for better clarity.</p>
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<p>(<b>A</b>) A typical map of the position of the PL peak of the InAlAs layer with pits. (<b>B</b>) Micro-PL spectra from the InAlAs layer measured (1) inside and (outside) the cluster. The annealing temperature of the substrate/growth is 535/505 °C.</p>
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<p>Experimental and calculated temperature dependencies of the pit depth (black square) and In depletion (red circle) for lattice-matched 1 μm thick InAlAs layers.</p>
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11 pages, 2655 KiB  
Article
Enhanced Optical and Electrical Properties of IGZO/Ag/IGZO for Solar Cell Application via Post-Rapid Thermal Annealing
by Chanmin Hwang, Taegi Kim, Yuseong Jang, Doowon Lee and Hee-Dong Kim
Nanomaterials 2024, 14(22), 1841; https://doi.org/10.3390/nano14221841 - 18 Nov 2024
Viewed by 2090
Abstract
In this paper, we optimized IGZO/Ag/IGZO (IAI) multilayer films by post-rapid thermal annealing (RTA) to enhance the electrical conductivity and optical transmittance in visible wavelengths for solar cell applications. Our optimized device showed an average transmittance of 85% in the visible range, with [...] Read more.
In this paper, we optimized IGZO/Ag/IGZO (IAI) multilayer films by post-rapid thermal annealing (RTA) to enhance the electrical conductivity and optical transmittance in visible wavelengths for solar cell applications. Our optimized device showed an average transmittance of 85% in the visible range, with a lowest sheet resistance of 6.03 Ω/□ when annealed at 500 °C for 60 s. Based on these results, we assessed our device with photo-generated short circuit current density (JSC) using a solar cell simulator to confirm its applicability in the solar cell. IAI multilayer RTA at 500 °C for 60 s showed a highest JSC of 40.73 mA/cm2. These results show that our proposed IAI multilayer film, which showed a high optical transparency and electrical conductivity optimized with post RTA, seems to be excellent transparent electrode for solar cell applications. Full article
(This article belongs to the Special Issue Nanostructured Materials for Electric Applications)
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<p>The RTA process for the IGZO/Ag/IGZO multilayer, and the right diagram describes the generated oxygen vacancies from the IGZO inside by RTA.</p>
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<p>AFM topology images of IGZO/Ag/IGZO after RTA, (<b>a</b>) RT, (<b>b</b>) 300, (<b>c</b>) 400, and (<b>d</b>) 500 °C for 60 s.</p>
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<p>The sheet resistance of (<b>a</b>) IGZO and (<b>b</b>) IGZO/Ag/IGZO multilayers after varying temperature conditions.</p>
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<p>(<b>a</b>) Impedance of IGZO/Ag/IGZO after RTA RT to 500 °C for 60 s and (<b>b</b>) equivalent circuit of IGZO/Ag/IGZO.</p>
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<p>(<b>a</b>) Transmittance, (<b>b</b>) reflectivity, and (<b>c</b>) absorption coefficient of IGZO/Ag/IGZO after RTA RT to 500 °C for 60 s, and each inset depicts the transmittance and reflectivity at 500 nm wavelength with varying annealing temperature.</p>
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<p>(<b>a</b>) Schematic structure of IGZO/Ag/IGZO-based solar cell and (<b>b</b>) the photo-generated short circuit current of IGZO/Ag/IGZO-based solar cell as a function of annealing temperature.</p>
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18 pages, 2873 KiB  
Article
Improving Resistive Heating, Electrical and Thermal Properties of Graphene-Based Poly(Vinylidene Fluoride) Nanocomposites by Controlled 3D Printing
by Rumiana Kotsilkova, Vladimir Georgiev, Mariya Aleksandrova, Todor Batakliev, Evgeni Ivanov, Giovanni Spinelli, Rade Tomov and Tsvetozar Tsanev
Nanomaterials 2024, 14(22), 1840; https://doi.org/10.3390/nano14221840 - 17 Nov 2024
Viewed by 1400
Abstract
This study developed a novel 3D-printable poly(vinylidene fluoride) (PVDF)-based nanocomposite incorporating 6 wt% graphene nanoplatelets (GNPs) with programmable characteristics for resistive heating applications. The results highlighted the significant effect of a controlled printing direction (longitudinal, diagonal, and transverse) on the electrical, thermal, Joule [...] Read more.
This study developed a novel 3D-printable poly(vinylidene fluoride) (PVDF)-based nanocomposite incorporating 6 wt% graphene nanoplatelets (GNPs) with programmable characteristics for resistive heating applications. The results highlighted the significant effect of a controlled printing direction (longitudinal, diagonal, and transverse) on the electrical, thermal, Joule heating, and thermo-resistive properties of the printed structures. The 6 wt% GNP/PVDF nanocomposite exhibited a high electrical conductivity of 112 S·m−1 when printed in a longitudinal direction, which decreased significantly in other directions. The Joule heating tests confirmed the material’s efficiency in resistive heating, with the maximum temperature reaching up to 65 °C under an applied low voltage of 2 V at a raster angle of printing of 0°, while the heating Tmax decreased stepwise with 10 °C at the 45° and the 90° printing directions. The repeatability of the Joule heating performance was verified through multiple heating and cooling cycles, demonstrating consistent maximum temperatures across several tests. The effect of sample thickness, controlled by the number of printed layers, was investigated, and the results underscore the advantages of programmable 3D printing orientation in thin layers for enhanced thermal stability, tailored electrical conductivity, and efficient Joule heating capabilities of 6 wt% GNP/PVDF composites, positioning them as promising candidates for next-generation 3D-printed electronic devices and self-heating applications. Full article
(This article belongs to the Special Issue Hybrid Nano Polymer Composites (2nd Edition))
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<p>TEM images: (<b>a</b>) GNP filler surfaces with SEAD pattern (inset); (<b>b</b>) high-resolution TEM image of the GNP thickness showing the multi-layered structure of oriented graphene monolayers; and (<b>c</b>) exfoliated GNP nanostructures dispersed in the PVDF matrix. Arrows show the thickness of the exfoliated GNPs.</p>
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<p>Thermal properties of PVDF and 6 wt% GNP/PVDF: DSC thermograms of heat flow vs. temperature at a scan rate of 10 °C/min, showing the first heating run (<b>a</b>), cooling cycle (<b>b</b>), and second heating run (<b>c</b>). The dash lines point the thermal transitions of the neat PVDF. In (<b>d</b>), the TGA/DTG thermograms of mass loss vs. temperature for the polymer and the nanocomposite are plotted, while the GNP thermogram is presented in the inset figure.</p>
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<p>SEM micrographs of the cut surface of samples with different deposition directions: (<b>a</b>) longitudinal (3DP 0°); (<b>b</b>) diagonal (3DP 45°); (<b>c</b>) transverse (3DP 90°); and (<b>d</b>) voltage vs. current dependence, varying the printing directions. The magnification bar is 1 mm. The arrows show the current flow direction.</p>
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<p>Comparison of (<b>a</b>) temperature vs. time and (<b>b</b>) temperature increase and heat vs. electrical conductivity of 6 wt% GNP/PVDF, varying the 3D printing directions—3DP 0°, 3DP 45°, and 3DP 90°—for 2 mm thick samples at an applied voltage of 2 V.</p>
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<p>Temperature vs. time for four-cycle heating–cooling test of 6 wt% GNP/PVDF samples at an applied voltage of 2 V with various printing directions: (<b>a</b>) longitudinal 3DP 0°, (<b>b</b>) diagonal 3DP 45°, and (<b>c</b>) transverse 3DP 90°. (<b>d</b>) Repeatability of the maximal temperature and current in the four heating–cooling cycles for the three printing directions.</p>
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<p>Temperature and current vs. time for 6 wt% GNP/PVDF, for the diagonally printed samples (3DP 45°) with (<b>a</b>) 4 printed layers (0.8 mm thick) and (<b>b</b>) 10 printed layers (2 mm thick), varying the applied voltage.</p>
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<p>Comparison of (<b>a</b>) maximum heating temperature and current vs. applied voltage and (<b>b</b>) generated heat and heating efficiency vs. power for the 3DP45° samples of the 6 wt% GNP/PVDF nanocomposite, with a controlled number of printed layers (4 layers, 0.8 mm thick; and 10 layers, 2 mm thick).</p>
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<p>Resistance vs. temperature of the 6 wt% GNP/PVDF composites with various printing directions of 3DP 0°, 3DP 45°, and 3DP 90°.</p>
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<p>Thermal diffusivity and conductivity of the 3DP samples of 6 wt% GNP/PVDF vs. temperature, with various printing directions.</p>
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45 pages, 11195 KiB  
Review
Exploring Plasmonic Standalone Surface-Enhanced Raman Scattering Nanoprobes for Multifaceted Applications in Biomedical, Food, and Environmental Fields
by Valentina Rojas Martínez, Eunseo Lee and Jeong-Wook Oh
Nanomaterials 2024, 14(22), 1839; https://doi.org/10.3390/nano14221839 - 17 Nov 2024
Cited by 1 | Viewed by 1721
Abstract
Surface-enhanced Raman scattering (SERS) is an innovative spectroscopic technique that amplifies the Raman signals of molecules adsorbed on rough metal surfaces, making it pivotal for single-molecule detection in complex biological and environmental matrices. This review aims to elucidate the design strategies and recent [...] Read more.
Surface-enhanced Raman scattering (SERS) is an innovative spectroscopic technique that amplifies the Raman signals of molecules adsorbed on rough metal surfaces, making it pivotal for single-molecule detection in complex biological and environmental matrices. This review aims to elucidate the design strategies and recent advancements in the application of standalone SERS nanoprobes, with a special focus on quantifiable SERS tags. We conducted a comprehensive analysis of the recent literature, focusing on the development of SERS nanoprobes that employ novel nanostructuring techniques to enhance signal reliability and quantification. Standalone SERS nanoprobes exhibit significant enhancements in sensitivity and specificity due to optimized hot spot generation and improved reporter molecule interactions. Recent innovations include the development of nanogap and core–satellite structures that enhance electromagnetic fields, which are crucial for SERS applications. Standalone SERS nanoprobes, particularly those utilizing indirect detection mechanisms, represent a significant advancement in the field. They hold potential for wide-ranging applications, from disease diagnostics to environmental monitoring, owing to their enhanced sensitivity and ability to operate under complex sample conditions. Full article
(This article belongs to the Special Issue Versatile Plasmonic Nanostructures for Biomedical Applications)
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<p>(<b>A</b>) SERS-based sensors: Direct SERS detection using the Raman signal of target molecules and indirect SERS detection using the Raman signal transformation of Raman reporter molecules (e.g., Raman reporter modified aptamer) or the amplified Raman signal of standalone SERS nanotags. (<b>B</b>) Various nanostructures for efficient standalone SERS nanoprobes.</p>
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<p>SERS mechanisms: (<b>A</b>) LSPR-induced EM enhancement. (<b>B</b>) CT resonance mechanism of CM enhancement mechanisms at a metal-molecule or semiconductor-molecule interface. The arrows indicate CT transitions (<span class="html-italic">μ</span><sub>CT</sub>), electronic transitions of a molecule (<span class="html-italic">μ</span><sub>mol</sub>), E<sub>F</sub> (Fermi level), HOMO (highest occupied molecular orbital), LUMO (lowest unoccupied molecular orbital), VB (valence band), and CB (conduction band).</p>
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<p>(<b>A</b>–<b>D</b>) Transmission electron microscopy (TEM) images of diverse morphologies of nanoparticles: (<b>A</b>) Au nanosphere (adapted with permission from [<a href="#B68-nanomaterials-14-01839" class="html-bibr">68</a>]; Copyright 2021 American Chemical Society). (<b>B</b>) Au nanotriangles (adapted with permission from [<a href="#B69-nanomaterials-14-01839" class="html-bibr">69</a>]; Copyright 2022 American Chemical Society). (<b>C</b>) Au nanocubes (adapted with permission from [<a href="#B70-nanomaterials-14-01839" class="html-bibr">70</a>]; Copyright 2022 Elsevier). (<b>D</b>) Au nanorods with various aspect ratios. The ratios of Au NRs are 5.9, 6.4, 6.4, 7.5, and 8.5, corresponing to Figures (<b>D</b>-<b>a</b>) through (<b>D</b>-<b>e</b>), respectively. (<b>D</b>-<b>f</b>) UV-vis-NIR spectra of Au NRs shown in (<b>D</b>-<b>a</b>) (black), (<b>D</b>-<b>b</b>) (green), (<b>D</b>-<b>c</b>) (red), (<b>D</b>-<b>d</b>) (blue), and (<b>D</b>-<b>e</b>) (magenta), respectively. The orange curve is the UV-vis-NIR spectrum of Au NRs synthesized with the ratio of 7.3. All scale bars represent 100 nm. (adapted with permission from [<a href="#B63-nanomaterials-14-01839" class="html-bibr">63</a>]; Copyright 2012 American Chemical Society). (<b>E</b>) TEM image of Ag@NO<sub>2</sub> (adapted with permission from [<a href="#B66-nanomaterials-14-01839" class="html-bibr">66</a>]; Copyright 2022 The Royal Society of Chemistry). (<b>F</b>) Au nanostars (adapted with permission from [<a href="#B67-nanomaterials-14-01839" class="html-bibr">67</a>]; Copyright 2012 IOP Publishing).</p>
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<p>(<b>A</b>) Au dimers with nanogaps bridged by metal-organic molecular cages (MOCs) of different sizes (MOC1, MOC2, and MOC3). (<b>A</b>-<b>a</b>) TEM images, (<b>A</b>-<b>b</b>) HRTEM images, and (<b>A</b>-<b>c</b>) simulated electric field distributions around the dimers. <b>1</b>, <b>2</b>, and <b>3</b> corresponds to MOC1, MOC2, and MOC3, respectively. (adapted with permission from REF [<a href="#B76-nanomaterials-14-01839" class="html-bibr">76</a>]; Copyright 2021 American Chemical Society). (<b>B</b>) DNA origami nanofork-based dimeric structures with various NPs (adapted with permission from REF [<a href="#B79-nanomaterials-14-01839" class="html-bibr">79</a>]; Copyright 2023 American Chemical Society). (<b>C</b>) Dimeric structure with a nanocube and a nanosphere (adapted with permission from REF [<a href="#B80-nanomaterials-14-01839" class="html-bibr">80</a>]; Copyright 2021 Wiley-VCH). (<b>D</b>) Au@Ag nanostar dimer (adapted with permission from REF [<a href="#B81-nanomaterials-14-01839" class="html-bibr">81</a>]; Copyright 2021 American Chemical Society). (<b>E</b>) Detection of endotoxin by SERS chip with dimeric SERS nanotags (adapted with permission from REF [<a href="#B83-nanomaterials-14-01839" class="html-bibr">83</a>]; Copyright 2020 American Chemical Society). (<b>F</b>) Raman imaging of cancer cells with Au dimers (adapted with permission from REF [<a href="#B84-nanomaterials-14-01839" class="html-bibr">84</a>]; Copyright 2017 American Chemical Society). (<b>G</b>) Au dimers, trimers, and comparison of their Raman signals (adapted with permission from REF [<a href="#B87-nanomaterials-14-01839" class="html-bibr">87</a>]; Copyright 2017 Royal Society of Chemistry) (<b>H</b>) DNA origami-based tetramer structure (adapted with permission from REF [<a href="#B86-nanomaterials-14-01839" class="html-bibr">86</a>]; Copyright 2014 American Chemical Society).</p>
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<p>(<b>A</b>) TEM images of Au@4-MBN@AgNPs with Ag shell thickness of 2.2, 3.6, 6.4, 8.9, 10.1, and 12.2 nm (adapted under the terms of CC-BY License from REF [<a href="#B91-nanomaterials-14-01839" class="html-bibr">91</a>]; Copyright 2024 The Authors, published in Frontiers). (<b>B</b>) Raman intensity of different shell thicknesses of Au@4-MBN@AgNPs at 2221cm<sup>−1</sup> (adapted under the terms of CC-BY License from REF [<a href="#B91-nanomaterials-14-01839" class="html-bibr">91</a>]; Copyright 2024 The Authors, published in Frontiers). (<b>C</b>) HRTEM images of Au@ATP@Ag nanorods obtained at a sub-threshold 4-ATP concentration CATP = 2.0 × 10<sup>−7</sup> M (adapted with permission from REF [<a href="#B92-nanomaterials-14-01839" class="html-bibr">92</a>]; Copyright 2016 Tsinghua University Press and Springer-Verlag GmbH Germany). (<b>D</b>) SERS spectra of the Au@Ag@ATP7 (left) and Au@ATP@Ag7 (right) samples before and after oxidation of the amino groups with hydrogen peroxide. The asterisk represents four additional peaks observed after oxidation, with three peaks at higher wavenumbers corresponding to nitrobenzene (adapted with permission from REF [<a href="#B92-nanomaterials-14-01839" class="html-bibr">92</a>]; Copyright 2016 Tsinghua University Press and Springer-Verlag GmbH Germany). (<b>E</b>) HRTEM images of Au/SiO<sub>2</sub> core–shell nanoparticles, SHINERS: shell-isolated mode and schematic of a SHINERS experiment on living yeast cells (adapted with permission from REF [<a href="#B93-nanomaterials-14-01839" class="html-bibr">93</a>]; Copyright 2010 Springer nature). (<b>F</b>) Schematic representation of H<sub>2</sub>O<sub>2</sub> triggered degradation of MnO<sub>2</sub> coating, TEM image, and evaluation MnO<sub>2</sub> degradation SERS fingerprinting (adapted with permission from REF [<a href="#B94-nanomaterials-14-01839" class="html-bibr">94</a>]; Copyright 2021 American Chemical Society).</p>
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<p>Synthetic schematic diagram (<b>A</b>) and electric field distribution (<b>B</b>) of SiO<sub>2</sub>@Au-Ag CJS (adapted with permission from REF [<a href="#B97-nanomaterials-14-01839" class="html-bibr">97</a>]; Copyright 2023 American Chemical Society). (<b>C</b>) Schematic diagram of SERS-ELISA platform with CS@SiO<sub>2</sub> core–satellite Au NPs (adapted with permission from REF [<a href="#B100-nanomaterials-14-01839" class="html-bibr">100</a>]; Copyright 2023 Elsevier). UV-vis spectra, TEM images (inset) (<b>D</b>), and SERS spectra (<b>E</b>) of the nanosensor before and after incubation with MMP-2. The characteristic peaks of DTNB (5,5′-dithiobis(2-nitrobenzoic acid)) at 1324 cm<sup>−1</sup> (red dash) and MBN (4-mercaptobenzonitrile) at 1580 cm<sup>−1</sup> (blue range) (adapted with permission from REF [<a href="#B103-nanomaterials-14-01839" class="html-bibr">103</a>]; Copyright 2024 American Chemical Society).</p>
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<p>(<b>A</b>) Calculated near-field EM field distribution of the Au-NNP and a silica-gapped Au-Au core-gap-shell nanoparticle without a bridge (adapted with permission from [<a href="#B104-nanomaterials-14-01839" class="html-bibr">104</a>]; Copyright 2011 Springer Nature). (<b>B</b>) TEM images of Au-NNP structures after Au shell formation on various DNA-modified Au cores (adapted with permission from [<a href="#B105-nanomaterials-14-01839" class="html-bibr">105</a>]; Copyright 2014 American Chemical Society). (<b>C</b>) Calculated near-field EM field distribution of Au-NNPs with different surface morphologies (adapted with permission from [<a href="#B107-nanomaterials-14-01839" class="html-bibr">107</a>]; Copyright 2016 Wiley-VCH). (<b>D</b>) P-GERTs and S-GERTs (adapted with permission from [<a href="#B110-nanomaterials-14-01839" class="html-bibr">110</a>]; Copyright 2019 Springer Nature). (<b>E</b>) Schematic diagram of high-speed cell Raman imaging and bright-field and Raman images of a single H1299 cell with different parts randomly selected (point 1–3). Scale bars are 10 μm (adapted with permission from [<a href="#B110-nanomaterials-14-01839" class="html-bibr">110</a>]; Copyright 2019 Springer Nature). (<b>F</b>) Progression of structural complexity in nanoframes with increasing chemical steps (adapted with permission from [<a href="#B114-nanomaterials-14-01839" class="html-bibr">114</a>]; Copyright 2023 American Chemical Society). (<b>G</b>) Synthetic scheme and TEM images of AuDGNs (adapted with permission from [<a href="#B115-nanomaterials-14-01839" class="html-bibr">115</a>]; Copyright 2016 Wiley-VCH). (<b>H</b>) OXNCs with different gap sizes and those HAADF-STEM images (i–iii). The scale bars indicate 100 nm (adapted with permission from [<a href="#B113-nanomaterials-14-01839" class="html-bibr">113</a>]; Copyright 2024 American Chemical Society). (<b>I</b>) Structures and sizes of hemin, myoglobin, and hemoglobin (adapted with permission from [<a href="#B113-nanomaterials-14-01839" class="html-bibr">113</a>]; Copyright 2024 American Chemical Society). (<b>J</b>) SERS spectra of hemin (green line) mixed with the OXNC with 2.6 nm gaps, myoglobin (blue line) with the OXNC with 5.6 nm gaps, and hemoglobin (orange line) mixed with the OXNC with 5.6 nm gaps (adapted with permission from [<a href="#B113-nanomaterials-14-01839" class="html-bibr">113</a>]; Copyright 2024 American Chemical Society).</p>
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<p>(<b>A</b>) ERA-SERS-LF strip (left) and phototgraphs (right, inset) and the calibration curve (Right) of SiO<sub>2</sub>@Au-based ERA-LF-SERS strips when testing the IAV DNA (adapted with permission from [<a href="#B120-nanomaterials-14-01839" class="html-bibr">120</a>]; Copyright 2023 American Chemical Society). (<b>B</b>) Clinical serum sample tests by Ag@Au NP-based dual-mode LFIA (adapted with permission from [<a href="#B121-nanomaterials-14-01839" class="html-bibr">121</a>]; Copyright 2022 American Chemical Society). (<b>C</b>) Schematic representation of assay. Total RNA is first isolated from samples before target RNA biomarkers are simultaneously amplified using isothermal reverse transcription-recombinase polymerase amplification. During amplification, amplicons are tagged with biotin molecules and target-specific overhang hybridization sequences. The different biomarker-specific amplicons are then labeled with respective SERS nanotags through complementary sequence hybridization and magnetically purified. Finally, the amplicons are detected by SERS concurrently, and quantitative analysis of biomarker level is derived from the spectral peak of each unique SERS nanotag. The Raman signals correspond to characteristic peaks from the five different dyes of the SERS nanotags, respectively. (Adapted with permission from [<a href="#B126-nanomaterials-14-01839" class="html-bibr">126</a>]; Copyright 2016 Wiley-VCH).</p>
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<p>(<b>A</b>) Multiplexed biomarker detection using ER, PR, and HER2 IgGs conjugated SERS nanotags (adapted with permission from [<a href="#B130-nanomaterials-14-01839" class="html-bibr">130</a>]; Copyright 2023 Elsevier). (<b>B</b>) Colors of Au<sub>13</sub>NPs, ASNPs, AS@mSiO<sub>2</sub> NPs, and pAS@AuNCs suspended in nanopure water with SPR peaks at 518, 700, 734, and 806 nm, respectively (adapted with permission from [<a href="#B131-nanomaterials-14-01839" class="html-bibr">131</a>]; Copyright 2023 Wiley-VCH). (<b>C</b>) Schematic illustration application of the multilayered mesoporous Au nanoarchitecture (RGD/DOX-pAS@AuNC) labeled with Raman reporter (MBA) via Au–thiol covalent bond for surface-enhanced Raman scattering (SERS) imaging-guided synergistic therapy toward cancer. (adapted with permission from [<a href="#B131-nanomaterials-14-01839" class="html-bibr">131</a>]; Copyright 2023 Wiley-VCH). (<b>D</b>) Schematic illustration showing that AuDAg<sub>2</sub>S nanoprobes equipped with SERS/NIR-II optical imaging could multidimensional tumor images from living subjects, pathology to the single-cell and further guided NIR-II deeper photothermal therapy (adapted with permission from [<a href="#B132-nanomaterials-14-01839" class="html-bibr">132</a>]; Copyright 2022 Wiley-VCH). (<b>E</b>) Fabrication of Oligonucleotide Modified Bioorthogonal SERS Nanotags (adapted with permission from [<a href="#B133-nanomaterials-14-01839" class="html-bibr">133</a>]; Copyright 2020 American Chemical Society). (<b>F</b>) Bioorthogonal SERS nanotags as a precision theranostic platform for cancer detection and photothermal therapy in mice after intravenous injection (adapted with permission from [<a href="#B133-nanomaterials-14-01839" class="html-bibr">133</a>]; Copyright 2020 American Chemical Society). (<b>G</b>) Photographic image of a BALB/c mouse with blank and <span class="html-italic">S. aureus</span> infected wounds after applying ACPA and SERS images at 2086 cm<sup>−1</sup> of <span class="html-italic">S. aureus</span> (right) and blank (left) infected wounds at different time points (left). Corresponding average SERS intensities of ACPA on wounds. *** <span class="html-italic">p</span> &lt; 0.001 (right) (adapted with permission from [<a href="#B134-nanomaterials-14-01839" class="html-bibr">134</a>]; Copyright 2023 American Chemical Society).</p>
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<p>(<b>A</b>) SERS spectral responses obtained from the reaction of the developed SERS aptasensor with various concentrations of pathogens (adapted with permission from [<a href="#B135-nanomaterials-14-01839" class="html-bibr">135</a>]; Copyright 2020 Elsevier). (<b>B</b>) Photographs of the LFIA strip with histamine (Hist), parvalbumin (Parv), and protein-G (PG) immobilized in the test (T) and control (<b>C</b>) lines, as indicated. SERS intensity mappings acquired at 1616 and 1646 cm<sup>−1</sup>, which are characteristic peaks of αHist-MGITC SERS or αParvRBITC SERS tags, respectively. (<b>C</b>) Average SERS spectra acquired from the different concentrations of histamine. (<b>D</b>) Average SERS spectra acquired from the different concentrations of Parvalbumin ((<a href="#nanomaterials-14-01839-f007" class="html-fig">Figure 7</a>B–D) adapted with permission from [<a href="#B136-nanomaterials-14-01839" class="html-bibr">136</a>]; Copyright 2024 American Chemical Society). (<b>E</b>) Photographs of competitive LFIA (CLFIA) strips at different concentrations of AFB<sub>1</sub>. The black arrow marks the T-line, indicating the visible LOD (i.e., 0.2 ng/mL) as determined by 12 independent users using only the naked eye. (<b>F</b>) Photographs (left) and SEM images (right) of the CLFIA strip membrane at the AFB<sub>1</sub> concentrations of (<b>i</b>) 0 ng/mL, (<b>ii</b>) 0.05 ng/mL, and (<b>iii</b>) 0.2 ng/mL. The blue arrows annotate Au-Ag alloy NPs-incorporated silica spheres captured in the T-line, with their number gradually decreasing as AFB<sub>1</sub> concentration increases. No nanoparticles are observed in (<b>iii</b>). ((<b>E</b>,<b>F</b>) adapted with permission from [<a href="#B139-nanomaterials-14-01839" class="html-bibr">139</a>]; Copyright 2023 American Chemical Society). (<b>G</b>) Scheme of the SERS microarray immunoassay for multiple mycotoxins (adapted with permission from [<a href="#B140-nanomaterials-14-01839" class="html-bibr">140</a>]; Copyright 2024 American Chemical Society).</p>
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<p>(<b>A</b>) Aptamer-based turn-off dual SERS sensor with AuNF-Au@tag@Ag@Au NP core-satellite assembly platform for MC-LR and MC-RR (L: leucine, R: arginine). (<b>B</b>) Optical brightfield image of <span class="html-italic">M. aeruginosa</span> UTEX LB 2385 cells. (<b>C</b>). MC-LR levels produced by <span class="html-italic">M. aeruginosa</span> UTEX LB 2385 (curve a) and <span class="html-italic">C. reinhardti</span> (curve b) over 7 consecutive days, as determined by the aptasensor ((<b>A</b>–<b>C</b>) adapted with permission from [<a href="#B141-nanomaterials-14-01839" class="html-bibr">141</a>]; Copyright 2021 American Chemical Society). (<b>D</b>) Schematic diagram of the optical setup of the SPR-SERS microscope and detecting strategy for Pb<sup>2+</sup> and Hg<sup>2+</sup> using single-particle Raman imaging (adapted with permission from [<a href="#B142-nanomaterials-14-01839" class="html-bibr">142</a>]; Copyright 2023 American Chemical Society). (<b>E</b>) SERS-based AMP immunoassay with magnetic separation (adapted with permission from [<a href="#B143-nanomaterials-14-01839" class="html-bibr">143</a>]; Copyright 2022 Royal Society of Chemistry). (<b>F</b>) Detection of series BPA actual samples using the SERS ICA (ICA: immunochromatographic assay) strips (adapted with permission from [<a href="#B144-nanomaterials-14-01839" class="html-bibr">144</a>]; Copyright 2022 Elsevier). (<b>G</b>) An image of the detected organs of a bivalve <span class="html-italic">Ruditapes philippinarum</span>, Au NS@polystyrene (PS) core@shell structures with Cy7 dyes, and typical SERS spectra measured from the organs of the clams exposed to SERS@PS for 24 h. (adapted with permission from [<a href="#B145-nanomaterials-14-01839" class="html-bibr">145</a>]; Copyright 2022 Royal Society of Chemistry).</p>
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<p>(<b>A</b>) Schematic illustration of the synthesis process of polydopamine@gold (PDA@Au) nanowaxberry and its SERS detection. (I) Deposition of Au seeds onto the surface of the PDA sphere, (II) the iodide ions assisted the growth of Au nanoshell on the PDA sphere, and (III) SERS detection of pesticides, pollutants, and explosives using nanowaxberry as a substrate (adapted with permission from [<a href="#B147-nanomaterials-14-01839" class="html-bibr">147</a>]; Copyright 2018 American Chemical Society). (<b>B</b>) Schematic of the SERS nanosensor for •OH detection and mechanism and detection of H<sub>2</sub>O<sub>2</sub> and •OH generation in water microdroplets (adapted with permission from [<a href="#B148-nanomaterials-14-01839" class="html-bibr">148</a>]; Copyright 2024 American Chemical Society).</p>
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12 pages, 5559 KiB  
Article
Potassium-Based Solid Sorbents for CO2 Adsorption: Key Role of Interconnected Pores
by Yuan Zhao, Jiangbo Huo, Xuefei Wang and Shunwei Ma
Nanomaterials 2024, 14(22), 1838; https://doi.org/10.3390/nano14221838 - 17 Nov 2024
Viewed by 885
Abstract
Industrial CO2 emissions contribute to pollution and greenhouse effects, highlighting the importance of carbon capture. Potassium carbonate (K2CO3) is an effective CO2 absorbent, yet its liquid-phase absorption faces issues like diffusion resistance and corrosion risks. In this [...] Read more.
Industrial CO2 emissions contribute to pollution and greenhouse effects, highlighting the importance of carbon capture. Potassium carbonate (K2CO3) is an effective CO2 absorbent, yet its liquid-phase absorption faces issues like diffusion resistance and corrosion risks. In this work, the solid adsorbents were developed with K2CO3 immobilized on the selected porous supports. Al2O3 had an optimum CO2 adsorption capacity of 0.82 mmol g−1. After further optimization of its pore structure, the self-prepared support Al2O3-2, which has an average pore diameter of 11.89 nm and a pore volume of 0.59 cm3 g−1, achieved a maximum CO2 adsorption capacity of 1.12 mmol g−1 following K2CO3 impregnation. Additionally, the relationship between support structure and CO2 adsorption efficiency was also analyzed. The connectivity of the pores and the large pore diameter of the support may play a key role in enhancing CO2 adsorption performance. During 10 cycles of testing, the K2CO3-based adsorbents demonstrated consistent high CO2 adsorption capacity with negligible degradation. Full article
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<p>Schematic diagram of the experimental setup for CO<sub>2</sub> adsorption assessment.</p>
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<p>CO<sub>2</sub> adsorption capacities of the 20% K<sub>2</sub>CO<sub>3</sub>/supports under the conditions: 10 vol% CO<sub>2</sub> in air, 298 K adsorption temperature.</p>
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<p>(<b>a</b>–<b>d</b>) CO<sub>2</sub> adsorption capacities of 20% K<sub>2</sub>CO<sub>3</sub>/Al<sub>2</sub>O<sub>3</sub>-2 adsorbents by varying preparation conditions.</p>
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<p>XRD patterns of Al<sub>2</sub>O<sub>3</sub>-1 and Al<sub>2</sub>O<sub>3</sub>-2.</p>
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<p>SEM images of Al<sub>2</sub>O<sub>3</sub>-1 (<b>a</b>,<b>b</b>) and Al<sub>2</sub>O<sub>3</sub>-2 (<b>c</b>,<b>d</b>).</p>
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<p>N<sub>2</sub> adsorption (hollow) and desorption (solid) isotherms of Al<sub>2</sub>O<sub>3</sub>-1 and Al<sub>2</sub>O<sub>3</sub>-2.</p>
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<p>Pore size distributions of Al<sub>2</sub>O<sub>3</sub>-1 and Al<sub>2</sub>O<sub>3</sub>-2.</p>
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<p>A comparative schematic of CO<sub>2</sub> diffusion in interconnected and non-interconnected pore channels. The arrow represents the direction of molecular diffusion.</p>
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<p>TGA curves of Al<sub>2</sub>O<sub>3</sub>-1 and Al<sub>2</sub>O<sub>3</sub>-2.</p>
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<p>Recycling performance of 20% K<sub>2</sub>CO<sub>3</sub>/Al<sub>2</sub>O<sub>3</sub>-2 adsorbent after 10 cycles.</p>
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19 pages, 6771 KiB  
Article
Enhancement of the Physical and Mechanical Properties of Cellulose Nanofibril-Reinforced Lignocellulosic Foams for Packaging and Building Applications
by Mara Paulette Alonso, Rakibul Hossain, Maryam El Hajam and Mehdi Tajvidi
Nanomaterials 2024, 14(22), 1837; https://doi.org/10.3390/nano14221837 - 17 Nov 2024
Viewed by 1498
Abstract
Biobased foams have the potential to serve as eco-friendly alternatives to petroleum-based foams, provided they achieve comparable thermomechanical and physical properties. We propose a facile approach to fabricate eco-friendly cellulose nanofibril (CNF)-reinforced thermomechanical pulp (TMP) fiber-based foams via an oven-drying process with thermal [...] Read more.
Biobased foams have the potential to serve as eco-friendly alternatives to petroleum-based foams, provided they achieve comparable thermomechanical and physical properties. We propose a facile approach to fabricate eco-friendly cellulose nanofibril (CNF)-reinforced thermomechanical pulp (TMP) fiber-based foams via an oven-drying process with thermal conductivity as low as 0.036 W/(m·K) at a 34.4 kg/m3 density. Acrodur®, iron chloride (FeCl3), and cationic polyacrylamide (CPAM) were used to improve the foam properties. Acrodur® did not have any significant effect on the foamability and density of the foams. Mechanical, thermal, cushioning, and water absorption properties of the foams were dependent on the density and interactions of the additives with the fibers. Due to their high density, foams with CPAM and FeCl3 at a 1% additive dosage had significantly higher compressive properties at the expense of slightly higher thermal conductivity. There was slight increase in compressive properties with the addition of Acrodur®. All additives improved the water stability of the foams, rendering them stable even after 24 h of water absorption. Full article
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<p>A schematic representation of the fabrication process of surfactant-assisted cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams.</p>
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<p>Stability of the aqueous foams (<b>a</b>) without any additive (neat foams), and with (<b>b</b>) 1% Acrodur<sup>®</sup>, (<b>c</b>) 1% CPAM, and (<b>d</b>) 1% FeCl<sub>3</sub> as additives. All additives were added at 1% of total fibers (based on dry weight). When fibers were used, the composition was 95% TMP fibers and 5% CNFs.</p>
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<p>Foamability values before and after adding thermomechanical pulp (TMP) fibers during gravity filtration for different formulations for the preparation of the cellulose nanofibril-reinforced TMP fiber-based foams.</p>
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<p>(<b>a</b>–<b>g</b>) Digital photographs of the cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams of different formulations and their respective thicknesses.</p>
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<p>(<b>a</b>) Density and (<b>b</b>) porosity of the cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams of different formulations. Values with common letters are not significantly different from each other at a significant level of 0.05.</p>
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<p>Scanning electron microscopy (SEM) images of the surfaces of the cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams with (<b>a</b>) no additives, (<b>b</b>) 1% Acrodur<sup>®</sup>, (<b>c</b>) 1% FeCl<sub>3</sub>, and (<b>d</b>) 1% CPAM as additives.</p>
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<p>Energy-dispersive X-ray spectroscopy (EDS) images of the surface of the cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams with (<b>a</b>) 0.5% FeCl<sub>3</sub> (<b>b</b>) 1% FeCl<sub>3</sub>, (<b>c</b>) 0.5% CPAM, and (<b>d</b>) 1% CPAM as additives.</p>
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<p>(<b>a</b>) Compressive strength at 10% and 25% strain, (<b>b</b>) compressive modulus, (<b>c</b>) thickness recovery after 35% compressive strain, and (<b>d</b>) foam resilience properties for cellulose nanofibrils-reinforced thermomechanical pulp fiber-based foams of different formulations. Values with common letters are not significantly different from each other at a significant level of 0.05.</p>
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<p>(<b>a</b>) Density, (<b>b</b>) tensile strain, normalized (<b>c</b>) tensile strength, and (<b>d</b>) tensile modulus of films (without SDS) with different additives. Values with common letters are not significantly different from each other at a significant level of 0.05.</p>
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<p>Scanning electron microscopy (SEM) images of the fractured surfaces of the cellulose nanofibrils-reinforced thermomechanical pulp fiber-based films with (<b>a</b>) no additive, (<b>b</b>) 1% Acrodur<sup>®</sup>, (<b>c</b>) 1% FeCl<sub>3</sub>, and (<b>d</b>) 1% CPAM as additives after tensile failure.</p>
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<p>(<b>a</b>) Water absorption (by volume) and (<b>b</b>) thickness swelling of the cellulose nanofibril-reinforced thermomechanical pulp fiber-based foams of different formulations for 2 h and 24 h test times. ‘X’ indicates disintegration of foams after water absorption. Values with common letters are not significantly different from each other at a significant level of 0.05.</p>
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<p>(<b>a</b>) Thermal conductivity and (<b>b</b>) the relationship between thermal conductivity and density of the cellulose nanofibrils-reinforced thermomechanical pulp fiber-based foams of different formulations. Values with common letters are not significantly different from each other at a significant level of 0.05.</p>
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15 pages, 3359 KiB  
Article
Improvement in Curcumin’s Stability and Release by Formulation in Flexible Nano-Liposomes
by Hua-Wei Chen, Su-Der Chen, Hung-Ta Wu, Chun-Hung Cheng, Chyow-San Chiou and Wei-Ting Chen
Nanomaterials 2024, 14(22), 1836; https://doi.org/10.3390/nano14221836 - 17 Nov 2024
Cited by 2 | Viewed by 1153
Abstract
Curcumin is utilized extensively as Chinese medicine in Asia due to its antioxidant, antimicrobial, and inflammatory activities. However, its use has the challenges of low oral bioavailability and high heat sensitivity. The aim of this research was to produce flexible nano-liposomes containing curcumin [...] Read more.
Curcumin is utilized extensively as Chinese medicine in Asia due to its antioxidant, antimicrobial, and inflammatory activities. However, its use has the challenges of low oral bioavailability and high heat sensitivity. The aim of this research was to produce flexible nano-liposomes containing curcumin using an innovative approach of ethanol injection and Tween 80 to enhance the stability and preservation of curcumin. The mean particle size, encapsulation efficiency, thermal degradation, storage stability, and curcumin release in flexible nano-liposomes were also investigated. We found that the mean particle size of curcumin-loaded flexible nano-liposome decreased from 278 nm to 27.6 nm. At the same time, the Tween 80 concentration increased from 0 to 0.15 wt%, which corresponded with the results of transmission electron microscopy (TEM) morphology analyses, and particle size decreased with an enhancement in Tween 80 concentration. Further, pure curcumin was quickly released within one hour at 37 °C, and first-order kinetics matched with its release curve. However, curcumin encapsulated in flexible nano-liposomes showed a slow release of 71.24% within 12 h, and a slower release pattern matched with the Higuchi model over 24 h, ultimately reaching 84.63% release. Hence, flexible nano-liposomes of curcumin made by a combination of ethanol injection and Tween 80 addition prevented the thermal degradation of curcumin, and enhanced its storage stability and preservation for future drug delivery applications. Full article
(This article belongs to the Special Issue Green Nanoparticles for Topical Administration of Drugs)
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<p>Transmission electron microscopy (TEM) images of flexible nano-liposomes loaded with curcumin prepared with different Tween 80 concentrations (<b>a</b>) 0.00 wt% (<b>b</b>) 0.05 wt% (<b>c</b>) 0.15 wt% (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL).</p>
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<p>The effect of different Tween 80 concentrations on flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL).</p>
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<p>Zeta potential of various liposome contents with and without Tween 80 (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>Degradation of curcumin at different temperatures with or without encapsulation in flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>Effects of different temperatures on curcumin liposomes and curcumin-loaded flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>Effects of different temperatures on curcumin liposomes and curcumin-loaded flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>The effect of soy lecithin concentrations on flexible nano-liposomes (cholesterol concentration: 0.15 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>The effect of cholesterol concentrations on flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; curcumin concentration: 0.20 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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<p>The effect of curcumin concentrations on curcumin-loaded flexible nano-liposomes (soy lecithin concentration: 12 mg/mL; cholesterol concentration: 0.15 mg/mL; Tween 80 concentration: 0.1 wt%).</p>
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17 pages, 3778 KiB  
Article
High-Performance Ammonia QCM Sensor Based on SnO2 Quantum Dots/Ti3C2Tx MXene Composites at Room Temperature
by Chong Li, Ran Tao, Jinqiao Hou, Huanming Wang, Chen Fu and Jingting Luo
Nanomaterials 2024, 14(22), 1835; https://doi.org/10.3390/nano14221835 - 16 Nov 2024
Viewed by 1124
Abstract
Ammonia (NH3) gas is prevalent in industrial production as a health hazardous gas. Consequently, it is essential to develop a straightforward, reliable, and stable NH3 sensor capable of operating at room temperature. This paper presents an innovative approach to modifying [...] Read more.
Ammonia (NH3) gas is prevalent in industrial production as a health hazardous gas. Consequently, it is essential to develop a straightforward, reliable, and stable NH3 sensor capable of operating at room temperature. This paper presents an innovative approach to modifying SnO2 colloidal quantum dots (CQDs) on the surface of Ti3C2Tx MXene to form a heterojunction, which introduces a significant number of adsorption sites and enhances the response of the sensor. Zero-dimensional (0D) SnO2 quantum dots and two-dimensional (2D) Ti3C2Tx MXene were prepared by solvothermal and in situ etching methods, respectively. The impact of the mass ratio between two materials on the performance was assessed. The sensor based on 12 wt% Ti3C2Tx MXene/SnO2 composites demonstrates excellent performance in terms of sensitivity and response/recovery speed. Upon exposure to 50 ppm NH3, the frequency shift in the sensor is −1140 Hz, which is 5.6 times larger than that of pure Ti3C2Tx MXene and 2.8 times higher than that of SnO2 CQDs. The response/recovery time of the sensor for 10 ppm NH3 was 36/54 s, respectively. The sensor exhibited a theoretical detection limit of 73 ppb and good repeatability. Furthermore, a stable sensing performance can be maintained after 30 days. The enhanced sensor performance can be attributed to the abundant active sites provided by the accumulation/depletion layer in the Ti3C2Tx/SnO2 heterojunction, which facilitates the adsorption of oxygen molecules. This work promotes the gas sensing application of MXenes and provides a way to improve gas sensing performance. Full article
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<p>Schematics of the synthesis of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites and preparation of ammonia QCM sensors.</p>
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<p>SEM images of (<b>a</b>) accordion-like Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> MXene, (<b>d</b>) SnO<sub>2</sub> CQDs, and (<b>g</b>) Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites. Inset of (<b>a</b>) is SEM image of MXene with few layers. HR-TEM images of (<b>b</b>,<b>c</b>) MXene, (<b>e</b>,<b>f</b>) SnO<sub>2</sub> CQDs, and (<b>h</b>) Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites. (<b>i</b>) SAED pattern of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites. (<b>j</b>) EDS map scanning analysis of Sn, O, Ti, and C elements.</p>
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<p>XRD patterns of the Ti<sub>3</sub>AlC<sub>2</sub> MAX phase, accordion-like Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> MXene, pure SnO<sub>2</sub> CQDs, and Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites.</p>
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<p>XPS spectra of (<b>a</b>) C 1s, (<b>b</b>) O 1s, (<b>c</b>) Sn 3d, and (<b>d</b>) Ti 2p.</p>
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<p>Response-time curves with different NH<sub>3</sub> concentrations based on (<b>a</b>) a Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> sensor, (<b>b</b>) a SnO<sub>2</sub> sensor, (<b>c</b>) a Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> sensor. (<b>d</b>) The curves between frequency shift and gas concentration of all sensors.</p>
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<p>(<b>a</b>) Frequency shift of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> sensor to NH<sub>3</sub> concentrations varying from 200 ppb to 8 ppm. Response and recovery curves of (<b>b</b>) SnO<sub>2</sub>, (<b>c</b>) Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>, and (<b>d</b>) Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites.</p>
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<p>(<b>a</b>) Repeated response of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> sensor to 10 ppm NH<sub>3</sub>. (<b>b</b>) Selectivity of sensor based on Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites. (<b>c</b>) Response curves of Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> sensor to 10 ppm of NH<sub>3</sub> at different relative humidities. (<b>d</b>) Long-term stability of sensor based on Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites.</p>
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<p>Energy band diagrams of SnO<sub>2</sub> and Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub> (<b>a</b>) before and (<b>b</b>) after contact. Schematic diagram of NH<sub>3</sub> sensing mechanism of sensor based on Ti<sub>3</sub>C<sub>2</sub>T<sub>x</sub>/SnO<sub>2</sub> composites, (<b>c</b>) in air, and (<b>d</b>) exposure to NH<sub>3</sub>.</p>
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15 pages, 5249 KiB  
Article
A Comprehensive Microstructure-Aware Electromigration Modeling Framework; Investigation of the Impact of Trench Dimensions in Damascene Copper Interconnects
by Ahmed Sobhi Saleh, Kristof Croes, Hajdin Ceric, Ingrid De Wolf and Houman Zahedmanesh
Nanomaterials 2024, 14(22), 1834; https://doi.org/10.3390/nano14221834 - 16 Nov 2024
Cited by 2 | Viewed by 769
Abstract
As electronic devices continue to shrink in size and increase in complexity, the current densities in interconnects drastically increase, intensifying the effects of electromigration (EM). This renders the understanding of EM crucial, due to its significant implications for device reliability and longevity. This [...] Read more.
As electronic devices continue to shrink in size and increase in complexity, the current densities in interconnects drastically increase, intensifying the effects of electromigration (EM). This renders the understanding of EM crucial, due to its significant implications for device reliability and longevity. This paper presents a comprehensive simulation framework for the investigation of EM in nano-interconnects, with a primary focus on unravelling the influential role of microstructure, by considering the impact of diffusion heterogeneity through the metal texture and interfaces. As such, the resulting atomic flux and stress distribution within nano-interconnects could be investigated. To this end, a novel approach to generate microstructures of the conductor metal is presented, whereby a predefined statistical distribution of grain sizes obtained from experimental texture analyses can be incorporated into the presented model, making the model predictive under various scales and working conditions with no need for continuous calibration. Additionally, the study advances beyond the state-of-the-art by comprehensively simulating all stages of electromigration including stress evolution, void nucleation, and void dynamics. The model was employed to study the impact of trench dimensions on the dual damascene copper texture and its impact on electromigration aging, where the model findings were corroborated by comparing them to the available experimental findings. A nearly linear increase in normalized time to nucleation was detected as the interconnect became wider with a fixed height for aspect ratios beyond 1. However, a saturation was detected with a further increase in width for lines of aspect ratios below 1, with no effective enhancement in time to nucleation. An aspect ratio of 1 seems to maximize the EM lifetime for a fixed cross-sectional area by fostering a bamboo-like structure, where about a 2-fold of increase was estimated when going from aspect ratio 2 to 1. Full article
(This article belongs to the Special Issue Mechanical and Thermal Properties of Nanomaterials)
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<p>A comparison between the atomic flux model in (<b>A</b>) the homogenous effective diffusivity approach [<a href="#B8-nanomaterials-14-01834" class="html-bibr">8</a>] and (<b>B</b>) the presented modeling approach in this work.</p>
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<p>The model utilized to generate grain microstructures. (<b>A</b>) The packed circles together with their weighted Voronoi tessellation. (<b>B</b>) The created grains from the tessellation after applying the grain boundary thickness. (<b>C</b>) The grain size distribution of the generated grains (orange histogram) shown together with the lognormal grain size distribution (continuous black curve).</p>
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<p>An example of the meshing scheme applied to our model. Two successive zoom-ins show how the mesh size varies from triple points to the middle of a grain boundary.</p>
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<p>A vector plot of the atomic flux when the electron flow is from left to right. The direction of the blue arrows indicates the atomic flux direction, and their lengths indicate the flux magnitudes.</p>
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<p>A colormap indicating the divergence of atomic flux through the diffusion path network. Divergence was non-existent along the path and had a positive or negative value at triple points depending on the type and angle of the path.</p>
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<p>A colormap plot to show the stress and the void’s geometry change with time. Two color bars are used for clarity, where the top bar has a small range to illustrate the subtle differences in stress along the grain’s boundaries and cap interfaces during the initial stress evolution phase (<b>A</b>–<b>D</b>). The bottom bar has a wide range to illustrate the drastic stress changes pre- and post-void nucleation (<b>E</b>–<b>H</b>). Multimedia is available online.</p>
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<p>(<b>A</b>) The stress evolution along the cap interface beyond the void nucleation time. Subplot shows the stress gradient at the void surface/cap intersection point and the current crowding factor at the void surface. (<b>B</b>) The simulated electromigration induced an increase in resistance with time, showing the three stages of electromigration aging.</p>
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<p>The time to nucleation normalized to the minimum value for different linewidths as estimated by our model vs. experimental results. For each simulation point, the average grain diameter, d, is shown together with a snapshot of the generated microstructure. Dashed vertical lines mark different aspect ratios. The temperature and rest of the working conditions in the simulations shown in this figure follow the reported values in [<a href="#B5-nanomaterials-14-01834" class="html-bibr">5</a>].</p>
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<p>The full scaling study showing time to nucleation at various linewidth and heights. Values were normalized w.r.t the (80,80) point. All simulation points along with a sigmoid fit (<b>left</b>). Interpolated surface shown by a colormap (<b>right</b>).</p>
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<p>The “p” factor calculated for different microstructures, generated by our calibrated microstructure generation module for different aspect ratios (black points), along with a sigmoid fit to give an analytical formula (blue line).</p>
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<p>Time to nucleation (normalized) vs. aspect ratio at different cross-sectional areas (<b>left</b>). Time to nucleation (normalized) vs. cross-sectional area at different aspect ratios (<b>right</b>). For each figure, an inset is given to show the lines of interest on the full scaling colormap.</p>
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<p>The EM-induced increase in resistance above the initial value as a function of time for different cross-sectional dimensions. Time 0 was defined as the time of void nucleation for each case.</p>
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21 pages, 2882 KiB  
Review
Gold Nanoprobes for Robust Colorimetric Detection of Nucleic Acid Sequences Related to Disease Diagnostics
by Maria Enea, Andreia Leite, Ricardo Franco and Eulália Pereira
Nanomaterials 2024, 14(22), 1833; https://doi.org/10.3390/nano14221833 - 16 Nov 2024
Viewed by 1489
Abstract
Gold nanoparticles (AuNPs) are highly attractive for applications in the field of biosensing, particularly for colorimetric nucleic acid detection. Their unique optical properties, which are highly sensitive to changes in their environment, make them ideal candidates for developing simple, rapid, and cost-effective assays. [...] Read more.
Gold nanoparticles (AuNPs) are highly attractive for applications in the field of biosensing, particularly for colorimetric nucleic acid detection. Their unique optical properties, which are highly sensitive to changes in their environment, make them ideal candidates for developing simple, rapid, and cost-effective assays. When functionalized with oligonucleotides (Au-nanoprobes), they can undergo aggregation or dispersion in the presence of complementary sequences, leading to distinct color changes that serve as a visual signal for detection. Aggregation-based assays offer significant advantages over other homogeneous assays, such as fluorescence-based methods, namely, label-free protocols, rapid interactions in homogeneous solutions, and detection by the naked eye or using low-cost instruments. Despite promising results, the application of Au-nanoprobe-based colorimetric assays in complex biological matrices faces several challenges. The most significant are related to the colloidal stability and oligonucleotide functionalization of the Au-nanoprobes but also to the mode of detection. The type of functionalization method, type of spacer, the oligo–AuNPs ratio, changes in pH, temperature, or ionic strength influence the Au-nanoprobe colloidal stability and thus the performance of the assay. This review elucidates characteristics of the Au-nanoprobes that are determined for colorimetric gold nanoparticles (AuNPs)-based nucleic acid detection, and how they influence the sensitivity and specificity of the colorimetric assay. These characteristics of the assay are fundamental to developing low-cost, robust biomedical sensors that perform effectively in biological fluids. Full article
(This article belongs to the Special Issue Noble Metal-Based Nanostructures: Optical Properties and Applications)
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<p>Timeline of AuNPs use for nucleic acid detection.</p>
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<p>Dependence of LSPR on spherical gold nanoparticles diameter and aggregation state.</p>
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<p>Colorimetric detection methods using spherical AuNPs: (Top panel) Cross-linking assay—a color change occurs as nucleic acid sequence strands specifically hybridize with complementary sequences, reducing the distance between particles, and resulting in a blue solution (positive test). In the absence of complementary sequences, the solution stays red (negative test). (Middle panel) Non-cross-linking assay—an increase in ionic strength induces AuNP aggregation, resulting in a blue solution (negative test). When complementary targets are present, the solution stays red (positive test). (Bottom panel) Colorimetric assay using unmodified AuNPs: In the absence of complementary sequences, only single-stranded DNA (ssDNA) is present, stabilizing AuNPs against salt-induced aggregation, and the solution stays red (negative result). Conversely, when hybridization occurs in the presence of a complementary sequence, double-stranded DNA (dsDNA) forms, and aggregation occurs (blue solution is a positive result). UV/vis spectra and Nanoparticle Tracking analysis (NTA) profiles are shown with blue lines corresponding to aggregated AuNPs samples and red lines to non-aggregated ones. Also indicated are the positive (green check) and negative (red cross) results for each test.</p>
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<p>Published successful functionalization methods of AuNPs with HS-oligos, resulting in Au-nanoprobes.</p>
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<p>Examples of Au nanoparticle interaction with (i) ssDNA, (ii) PolyA-ssDNA and PolyT-ssDNA, (iii) PEG-ssDNA, and (iv) thiolated-(CH2)6-ssDNA.</p>
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20 pages, 5333 KiB  
Article
Green Synthesis of Fe2O3 Nanoparticles Using Eucalyptus globulus Leaf Extract on Pinus radiata Sawdust for Cationic Dye Adsorption
by Pablo Salgado, Eduardo Aedo and Gladys Vidal
Nanomaterials 2024, 14(22), 1832; https://doi.org/10.3390/nano14221832 - 16 Nov 2024
Viewed by 957
Abstract
The present study reports the synthesis of Fe2O3 nanoparticles on Pinus radiata sawdust (Fe2O3@PS) using a Eucalyptus globulus leaf extract. The morphology and structure of Fe2O3@PS were characterized using scanning electron microscopy [...] Read more.
The present study reports the synthesis of Fe2O3 nanoparticles on Pinus radiata sawdust (Fe2O3@PS) using a Eucalyptus globulus leaf extract. The morphology and structure of Fe2O3@PS were characterized using scanning electron microscopy (SEM), X-ray diffraction (XRD), Fourier-transform infrared spectroscopy (FTIR), and UV–Vis diffuse reflectance. The adsorption capacity of the system was evaluated by testing its ability to remove the Rhodamine B (RhB) dye. The optimization of the system was carried out using the Plackett–Burman design (PBD) and the response surface methodology (steepest ascent and the Box–Behnken design), which provided information on the main parameters affecting the adsorption process. The PBD results showed that the most important parameters for the removal of RhB using Fe2O3@PS were the removal time, the RhB concentration, and the initial pH of the system. The reusability of Fe2O3@PS under optimal conditions was tested and it was found to maintain its efficiency after five cycles of use. The efficiency and rate of RhB removal observed at pH values near 7.0 were found to be predominantly influenced by electrostatic interactions. In contrast, the analyses conducted at pH values near 8.3 exhibited reduced influence from electrostatic attractions, with π–π interactions and hydrogen bonds emerging as dominant forces. At pH values exceeding 8.3, all potential interactions between RhB and Fe2O3@PS exhibited diminished strength. This research provides valuable information on the formation of eco-friendly nanoparticles immobilized on a forest residue such as sawdust, which can effectively remove organic pollutants like RhB. This contributes to the valorization of resources and the search for solutions to water pollution. Full article
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<p>Photographic images of (<b>a</b>) pristine PS, and (<b>b</b>) Fe<sub>2</sub>O<sub>3</sub>@PS.</p>
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<p>SEM images of (<b>a</b>) Pristine PS, (<b>b</b>) Fe<sub>2</sub>O<sub>3</sub>@PS, and (<b>c</b>) histogram of Fe<sub>2</sub>O<sub>3</sub>@PS sizes.</p>
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<p>DRX analysis of (<b>a</b>) pristine PS and (<b>b</b>) Fe<sub>2</sub>O<sub>3</sub>@PS.</p>
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<p>FTIR analyses for pristine PS and Fe<sub>2</sub>O<sub>3</sub>@PS (The black dotted line indicates a decline in signal intensity, the green dotted line represents a shift in wavenumber, and the blue dotted line denotes the disappearance of a signal).</p>
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<p>Absorption spectra of Fe<sub>2</sub>O<sub>3</sub>@PS and PS.</p>
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<p>Pareto chart showing the standardized effects of variables on RhB adsorption.</p>
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<p>Residual diagnostics of the quadratic model. (<b>a</b>) normal probability plot of residuals, (<b>b</b>) residuals against the predicted values of the model, (<b>c</b>) actual and predicted values of RhB adsorption (%) based on BBD.</p>
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<p>Effect of (<b>a</b>) time, (<b>b</b>) RhB concentration, and (<b>c</b>) pH on the adsorption efficiency of RhB.</p>
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<p>Determination of pHpzc for Fe<sub>2</sub>O<sub>3</sub>@PS using pH drift method.</p>
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<p>Three-dimensional response surface plots representing the modeled RhB adsorption (%) as a function of (<b>a</b>) time and RhB concentration, (<b>b</b>) time and pH, and (<b>c</b>) RhB concentration and pH.</p>
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<p>Reusability study of RhB adsorption using Fe<sub>2</sub>O<sub>3</sub>@PS by (<b>a</b>) conditions 1, and (<b>b</b>) conditions 2. The data obtained are presented as mean ± standard deviation.</p>
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<p>(<b>a</b>) RhB adsorption efficiency by Fe<sub>2</sub>O<sub>3</sub>@PS at different time intervals. (<b>b</b>) Calculated RhB adsorption rate constant (k<sub>app</sub>) for Fe<sub>2</sub>O<sub>3</sub>@PS (inset: legend represents k<sub>app</sub> and r<sup>2</sup> of a pseudo-first order model).</p>
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<p>Possible interactions in the RhB adsorption process using Fe<sub>2</sub>O<sub>3</sub>@PS under optimal conditions.</p>
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13 pages, 7273 KiB  
Article
Catalytic Methane Decomposition on In Situ Reduced FeCo Alloy Catalysts Derived from Layered Double Hydroxides
by Dianfeng Cao, Yuwen Li, Chao Lv, Yongtao An, Jiangfeng Song, Mingcan Li and Xin Zhang
Nanomaterials 2024, 14(22), 1831; https://doi.org/10.3390/nano14221831 - 15 Nov 2024
Viewed by 701
Abstract
Catalytic methane decomposition (CMD) reaction is considered a promising process for converting greenhouse gas CH4 into hydrogen and high-value-added carbon materials. In this work, a series of Al2O3-supported FeCo alloy catalysts were successfully prepared in the CMD process. [...] Read more.
Catalytic methane decomposition (CMD) reaction is considered a promising process for converting greenhouse gas CH4 into hydrogen and high-value-added carbon materials. In this work, a series of Al2O3-supported FeCo alloy catalysts were successfully prepared in the CMD process. Compared to the pre-reduced catalysts, the in situ reduced FeCo alloy catalysts showed higher methane conversion rates, with the highest reaching 83% at 700 °C, due to the finer active nanoparticle size and greater exposure of active site. Furthermore, the time-on-stream tests demonstrated that the catalytic activity of in situ reduced FeCo alloy catalysts could remain above 92.3% of the highest catalytic activity after 10 h. In addition, TEM analyses of the carbon products from the CMD in situ reduced catalysts revealed the production of carbon nanofibers and nanotubes several microns in length after the reaction. This indicates that the in situ reduced FeCo alloy catalysts more effectively promoted the growth of carbon nanofibers. These results could provide a viable strategy for future methane decomposition development aimed at producing hydrogen and high-value carbon. Full article
(This article belongs to the Special Issue Nanomaterials for Sustainable Green Energy)
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<p>(<b>a</b>) XRD patterns of FeCoAl-LDH-<span class="html-italic">x</span> and (<b>b</b>) XRD patterns of FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>.</p>
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<p>TEM images of (<b>a</b>–<b>c</b>) FeCoAl-LDH-<span class="html-italic">x</span> (<span class="html-italic">x</span> = 1–3). (<b>d</b>–<b>f</b>) TEM images of FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span> (<span class="html-italic">x</span> = 1–3). (<b>g</b>–<b>i</b>) Statistical distribution graphs of the particle size of FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span> (<span class="html-italic">x</span> = 1–3).</p>
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<p>(<b>a</b>) TG analysis of the FeCoAl-LDH-<span class="html-italic">x</span>, (<b>b</b>) the differential curves of TG about FeCoAl-LDH-<span class="html-italic">x</span>, (<b>c</b>) TG analysis of the FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>, and (<b>d</b>) the differential curves of TG about FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>.</p>
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<p>The relationship between methane conversion and temperature in the TPSR test at 5 °C/min to 800 °C for (<b>a</b>) FeCoAl-LDH-<span class="html-italic">x</span> and (<b>b</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>, and the relationship between methane conversion and temperature in the TOS test at 5 °C/min to 700 °C for insulation of (<b>c</b>) FeCoAl-LDH-<span class="html-italic">x</span> and (<b>d</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>.</p>
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<p>XRD patterns of methane decomposition reaction products catalyzed by (<b>a</b>) FeCoAl-LDH-<span class="html-italic">x</span> and (<b>b</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span>.</p>
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<p>TEM images of carbon products created by (<b>a</b>,<b>b</b>) FeCoAl-LDH-1, (<b>c</b>,<b>d</b>) FeCoAl-LDH-2, (<b>e</b>,<b>f</b>) and FeCoAl-LDH-3.</p>
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<p>TEM images of TG products created by (<b>a</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-1, (<b>b</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-2, and (<b>c</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-3.</p>
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<p>Raman spectra of (<b>a</b>) spent FeCoAl-LDHs-<span class="html-italic">x</span> (<span class="html-italic">x</span> = 1–3) and (<b>b</b>) FeCo/Al<sub>2</sub>O<sub>3</sub>-<span class="html-italic">x</span> (<span class="html-italic">x</span> = 1–3) catalysts after TG.</p>
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14 pages, 7597 KiB  
Article
Magnetic Field/Ultrasound-Responsive Fe3O4 Microbubbles for Targeted Mechanical/Catalytic Removal of Bacterial Biofilms
by Liang Lu, Yuan Liu, Xiaolong Chen, Fengjiao Xu, Qi Zhang, Zhaowei Yin and Lihui Yuwen
Nanomaterials 2024, 14(22), 1830; https://doi.org/10.3390/nano14221830 - 15 Nov 2024
Cited by 1 | Viewed by 975
Abstract
Conventional antibiotics are limited by drug resistance, poor penetration, and inadequate targeting in the treatment of bacterial biofilm-associated infections. Microbubble-based ultrasound (US)-responsive drug delivery systems can disrupt biofilm structures and enhance antibiotic penetration through cavitation effects. However, currently developed US-responsive microbubbles still depend [...] Read more.
Conventional antibiotics are limited by drug resistance, poor penetration, and inadequate targeting in the treatment of bacterial biofilm-associated infections. Microbubble-based ultrasound (US)-responsive drug delivery systems can disrupt biofilm structures and enhance antibiotic penetration through cavitation effects. However, currently developed US-responsive microbubbles still depend on antibiotics and lack targeting capability. In this work, magnetic field/ultrasound (MF/US)-responsive Fe3O4 microbubbles (FMB) were constructed based on Fe3O4 nanoparticles (NPs) with superparamagnetic and peroxidase-like catalytic properties. In vitro experiments demonstrated that FMB can be targeted to methicillin-resistant Staphylococcus aureus (MRSA) biofilms by the direction of MF. Upon US irradiation, FMB collapse due to inertial cavitation and generate mechanical forces to disrupt the structure of MRSA biofilms and releases Fe3O4 NPs, which catalyze the generation of reactive oxygen species (ROS) from H2O2 in the biofilm microenvironment and kill the bacteria within the biofilm. In a mouse biofilm infection model, FMB efficiently destroyed MRSA biofilms grown in subcutaneous catheters with the MF and US. Magnetic-targeted mechanical/catalytic therapy based on FMB provides a promising strategy for effectively combating bacterial biofilm infection. Full article
(This article belongs to the Special Issue Stimuli-Responsive Nanomaterials for Imaging and Therapy)
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<p>Schematic diagram of magnetic field/ultrasound (MF/US)-responsive Fe<sub>3</sub>O<sub>4</sub> microbubbles (FMB) for bacterial biofilm removal. (<b>a</b>) Mechanism of action of FMB for MF-targeted mechanical/catalytic removal of bacterial biofilms. (<b>b</b>) FMB target the MRSA biofilm of mouse subcutaneous catheter under the guidance of MF, destroy the biofilm structure by ultrasound cavitation effect, and catalyze the production of ROS from H<sub>2</sub>O<sub>2</sub> to kill the bacteria in the biofilm.</p>
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<p>Preparation and characterization of FMB. (<b>a</b>) Schematic of the preparation process of FMB. (<b>b</b>) Bright-field microphotograph of FMB. (<b>c</b>) Size distribution histogram of FMB with a statistical number greater than 200. (<b>d</b>) Content of Fe in different volumes of FMB aqueous dispersion. (<b>e</b>) Scanning electron microscopy (SEM) images and elemental mapping images of FMB. (<b>f</b>) X-ray diffraction (XRD) spectra of Fe<sub>3</sub>O<sub>4</sub> NPs, FMB, and standard powder diffraction pattern of Fe<sub>3</sub>O<sub>4</sub> (PDF#04-006-0424).</p>
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<p>MF/US-responsive properties of FMB. (<b>a</b>) Photographs of FMB before and after ultrasound irradiation. (<b>b</b>) Photographs of FMB before and after the action of MF. (<b>c</b>) Vibrating sample magnetometer (VSM) spectra of FMB. (<b>d</b>) Photographs of FMB migrating to the target position in the catheter under the action of a permanent magnet. t1, t2, t3, and t4 represent different time points. The red arrow indicates the moving direction of FMB.</p>
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<p>Catalytic properties of FMB. (<b>a</b>) Photographs of FMB catalyzing TMB in a Petri dish containing 300 mM H<sub>2</sub>O<sub>2</sub>. P1 and P2 represent the locations of FMB at different time points. The yellow arrow indicates the moving path of FMB. (<b>b</b>) Ultraviolet-visible-near-infrared (UV-vis-NIR) absorption spectra of FMB dispersions after reaction with TMB under different conditions; insets from left to right are photographs of TMB + H<sub>2</sub>O<sub>2</sub>, TMB + H<sub>2</sub>O<sub>2</sub> + FMB, and TMB + H<sub>2</sub>O<sub>2</sub> + FMB + US groups.</p>
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<p>MRSA biofilm disruption by FMB under MF and US. (<b>a</b>) Optical photographs, (<b>b</b>) microphotographs, and (<b>c</b>) relative biofilm biomass of MRSA biofilms after crystal violet staining with different treatments.</p>
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<p>MRSA biofilm disruption by FMB under MF and US at different concentrations of H<sub>2</sub>O<sub>2</sub>. (<b>a</b>) Optical photographs, (<b>b</b>) microphotographs, and (<b>c</b>) relative biofilm biomass of MRSA biofilms grown in 96-well plates with crystal violet staining after different treatments.</p>
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<p>Fluorescence imaging of MRSA biofilms. (<b>a</b>) Three-dimensional confocal laser scanning microscopy (3D CLSM) photographs of MRSA biofilms stained by Calcein–AM after different treatments. (<b>b</b>) Thickness of MRSA biofilms after different treatments. *** <span class="html-italic">p</span> &lt; 0.001.</p>
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<p>Antibacterial effect of FMB against MRSA biofilms. (<b>a</b>) Photographs of MRSA colonies on agar plates and (<b>b</b>) the number of viable bacteria in MRSA biofilms after different treatments. *** <span class="html-italic">p</span> &lt; 0.001.</p>
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<p>In vivo catheter MRSA biofilm clearance by FMB. (<b>a</b>) Schematic of the treatment of catheter biofilms in mice. (<b>b</b>) Photographs of crystal violet-stained and (<b>c</b>) relative biofilm biomass of catheters after different treatments. (<b>d</b>) MRSA colonies on agar plates and (<b>e</b>) number of viable bacteria within MRSA biofilm. ** <span class="html-italic">p</span> &lt; 0.01, and *** <span class="html-italic">p</span> &lt; 0.001.</p>
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