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Search Results (388)

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Keywords = silver doping

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14 pages, 1255 KiB  
Article
Impact of Diamond-like Carbon Films on Reverse Torque: Superior Performance in Implant Abutments with Internal Conical Connections
by Arianne Vallim Pinto Coelho, Viviane Maria Gonçalves de Figueiredo, Leandro Lameirão Ferreira, Alecsandro de Moura Silva, Marcelo Gallo Oliani, José Renato Cavalcanti de Queiroz, Argemiro Soares da Silva Sobrinho, Lafayette Nogueira Junior and Renata Falchete do Prado
Coatings 2024, 14(9), 1168; https://doi.org/10.3390/coatings14091168 - 10 Sep 2024
Viewed by 323
Abstract
The loosening or fracture of the prosthetic abutment screw is the most frequently reported complication in implant dentistry. Thin diamond-like carbon (DLC) films offer a low friction coefficient and high wear resistance, functioning as a solid lubricant to prevent the weakening of the [...] Read more.
The loosening or fracture of the prosthetic abutment screw is the most frequently reported complication in implant dentistry. Thin diamond-like carbon (DLC) films offer a low friction coefficient and high wear resistance, functioning as a solid lubricant to prevent the weakening of the implant–abutment system. This study evaluated the effects of DLC nanofilms on the reverse torque of prosthetic abutments after simulated chewing. Abutments with 8° and 11° taper connections, with and without DLC or silver-doped DLC coatings, were tested. The films were deposited through the plasma enhanced chemical vapor deposition process. After two million cycles of mechanical loading, reverse torque was measured. Analyses with scanning electron microscopy were conducted on three samples of each group before and after mechanical cycling to verify the adaptation of the abutments. Tribology, Raman and energy-dispersive spectroscopy analyses were performed. All groups showed a reduction in insertion torque, except the DLC-coated 8° abutments, which demonstrated increased reverse torque. The 11° taper groups experienced the most torque loss. The nanofilm had no significant effect on maintaining insertion torque, except for the DLC8 group, which showed improved performance. Full article
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Figure 1

Figure 1
<p>Boxplot of the relative difference (%) of the torque values (<b>A</b>). Column graph of the average relative difference (%) of the torque values (<b>B</b>).</p>
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<p>Thread images of C8 pre-cycling (<b>A</b>), post-cycling (<b>B</b>), DLC8 pre-cycling (<b>C</b>), and post-cycling (<b>D</b>) at 90× magnification in SE mode.</p>
Full article ">Figure 3
<p>Raman spectra of silver doped Ag-DLC (in black) and undoped DLC (in red). The presence of silver on the film changes the position and the intensities of the bands G that compose each spectrum. Raman spectra revealed that the G band is larger in the DLC film. The spectra include the fitting curves. Blue curve indicates the Lorentzian curves for the G-band without Gaussian convolution. Yellow curve indicates the Lorentzian curves for the D-band without the same Gaussian convolution.</p>
Full article ">
24 pages, 11966 KiB  
Review
Photodegradation of Amoxicillin in Aqueous Systems: A Review
by Mohammad Ashraf Ali and Ibrahim M. Maafa
Int. J. Mol. Sci. 2024, 25(17), 9575; https://doi.org/10.3390/ijms25179575 - 4 Sep 2024
Viewed by 286
Abstract
Amoxicillin (AMX) is utilized in the treatment of several infectious diseases, and its concentration in wastewater has increased quite significantly over the years, posing high health hazards for humans and other living organisms. Investigations are in progress globally to eliminate AMX and other [...] Read more.
Amoxicillin (AMX) is utilized in the treatment of several infectious diseases, and its concentration in wastewater has increased quite significantly over the years, posing high health hazards for humans and other living organisms. Investigations are in progress globally to eliminate AMX and other related pollutants using several methods that include adsorption, photolysis, photocatalytic degradation, photoelectrocatalytic degradation, and electrochemical conversion. AMX can be eliminated efficiently from the environment using photodegradation, either by photolysis or a photocatalytic process. Several types of semiconductor NMs have been used to eliminate AMX and other related drugs present in wastewater. This review spans the photodegradation studies conducted during the years 2018–2024 to degrade and eliminate AMX in aquatic systems. Several studies have been reported to eliminate AMX from different water streams. These studies are categorized into TiO2-containing and non-TiO2-based catalysts for better comparison. A section on photolysis is also included, showing the use of UV alone or with H2O2 or PS without using any nanomaterial. A tabulated summary of both types of catalysts showing the catalysts, reaction conditions, and degradation efficiency is presented. Researchers have used a variety of reaction conditions that include radiation types (UV, solar, and visible), pH of the solution, concentration of AMX, number of nanomaterials, presence of other additives and activators such as H2O2 as oxidant, and the influence of different salts like NaCl and CaCl2 on the photodegradation efficiency. TiO2 was the best nanomaterial found that achieved the highest degradation of AMX in ultraviolet irradiation. TiO2 doped with other nanomaterials showed very good performance under visible light. WO3 was also used by several investigators and found quite effective for AMX degradation. Other metal oxides used for AMX elimination were derived from molybdenum, zinc, manganese, copper, cerium, silver, etc. Some researchers have used UV and/or visible irradiation or sunlight, without using solid catalysts, in the presence of oxidants such as H2O2. A summarized description of earlier published reviews is also presented. Full article
(This article belongs to the Special Issue Recent Advances in Photolysis and Photodegradation)
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Figure 1

Figure 1
<p>A comparison of AMX degradation under different experimental conditions. (<b>A</b>) Degradation plots of AMX with TiO<sub>2</sub> anatase and kaolinite under light and dark conditions. (<b>B</b>) pH variation of the AMX as a function of reaction time [<a href="#B16-ijms-25-09575" class="html-bibr">16</a>].</p>
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<p>Interaction of AMX with the mineral surface and degradation into simpler products [<a href="#B16-ijms-25-09575" class="html-bibr">16</a>].</p>
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<p>Proposed degradation reactions of AMX under dark and solar radiation without minerals [<a href="#B16-ijms-25-09575" class="html-bibr">16</a>].</p>
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<p>Visualization of 2D/2D TiO<sub>2</sub>/Bi<sub>2</sub>MoO<sub>6</sub> catalyst and AMX photodegradation process [<a href="#B17-ijms-25-09575" class="html-bibr">17</a>].</p>
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<p>Photocatalytic degradation of AMX at different initial concentrations of 10 to 50 ppm using 0.2 g/L of catalyst at 25 °C [<a href="#B22-ijms-25-09575" class="html-bibr">22</a>].</p>
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<p>AMX photodegradation efficiency under UV and visible light. (A) No photocatalyst, (B) TiO<sub>2</sub>, and (C) Cu-TiO<sub>2</sub>. (AMX solution volume 100 mL, AMX concentration 10 mg/L, photocatalysts 40 mg, irradiation time 24 h, and pH 6) [<a href="#B27-ijms-25-09575" class="html-bibr">27</a>].</p>
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<p>Effect of pH on the degradation efficiency of AMX and cephalexin (CPX) under UV irradiation using ZnO, TiO<sub>2,</sub> and GO-Fe<sub>3</sub>O<sub>4</sub> catalyst. Irradiation time 20 min, catalyst 1 g/L, antibiotics 5 mg/L, UV radiation intensity 6 W [<a href="#B28-ijms-25-09575" class="html-bibr">28</a>].</p>
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<p>Effect of radiation intensity on the degradation efficiency of AMX, cephalexin (CPX), and tetracycline (TCN) under UV irradiation using ZnO, TiO<sub>2,</sub> and GO-Fe<sub>3</sub>O<sub>4</sub> catalysts: pH (AMX, CPX, TCN with GO-Fe<sub>3</sub>O<sub>4</sub>) unset; pH (AMX, CPX, TCN with TiO<sub>2</sub> or ZnO) 5, 7, 5; time (AMX, CPX, and TCN/MGO) 45, 45, 15 min; time (AMX, CPX, and TCN/TiO<sub>2</sub> or ZnO) 15, 45, 45 min; MGO quantity (with AMX, CPX, or TCN) 4, 4, 2 g/L; TiO<sub>2</sub> or ZnO quantity (with AMX, CPX, or TCN) 2, 2, 2 g/L; antibiotics concentration 15 mg/L [<a href="#B28-ijms-25-09575" class="html-bibr">28</a>].</p>
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<p>Effect of initial AMX concentrations on the degradation efficiency for 200 mL solution containing 100 mg/L and 300 mg/L AMX with 0.5 g CaTiO<sub>3</sub> at room temperature at different irradiation times [<a href="#B29-ijms-25-09575" class="html-bibr">29</a>].</p>
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<p>AMX degradation efficiency of 200 mL solution containing 100 mg/L AMX with 0.5 g CaTiO<sub>3</sub> at room temperature at different irradiation times at pH 3, 7, and 10 [<a href="#B29-ijms-25-09575" class="html-bibr">29</a>].</p>
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<p>Effect of CaTiO<sub>3</sub> amount on the AMX degradation efficiency for 200 mL aqueous solution having 100 mg/L AMX at pH 3 and room temperature [<a href="#B29-ijms-25-09575" class="html-bibr">29</a>].</p>
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<p>Effect of temperature on the AMX degradation efficiency for 200 mL solution having 100 mg/L AMX with 0.5 g CaTiO<sub>3</sub> and 0.058 g NaCl at pH 3 [<a href="#B29-ijms-25-09575" class="html-bibr">29</a>].</p>
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<p>Process of AMX degradation using TiO<sub>2</sub> under UV irradiation (UVA 365 nm, 672 W/m<sup>2</sup>) for 30 mg/L AMX concentration, TiO<sub>2</sub> dosage of 450 mg/L, H<sub>2</sub>O<sub>2</sub> concentration of 150 mg/L at pH 7.0 [<a href="#B30-ijms-25-09575" class="html-bibr">30</a>].</p>
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<p>(<b>a</b>) Possible mechanism of AMX degradation at the GO/TiO<sub>2</sub> surface [<a href="#B31-ijms-25-09575" class="html-bibr">31</a>]. Photocatalytic degradation kinetics of AMX by the synthesized materials under (<b>b</b>) visible light and (<b>c</b>) simulated solar light. (<b>d</b>) AMX degradation rate constants under solar and visible light [<a href="#B32-ijms-25-09575" class="html-bibr">32</a>].</p>
Full article ">Figure 15
<p>SEM images of photocatalysts (<b>a</b>) MIL-53(Al)/ZnO, (<b>b</b>) MIL-53Al, and (<b>c</b>) ZnO [<a href="#B38-ijms-25-09575" class="html-bibr">38</a>].</p>
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<p>Photodegradation results of AMX using different catalysts, using 50 mg/L of AMX and 0.6 g/L of catalyst at pH 7.0 [<a href="#B38-ijms-25-09575" class="html-bibr">38</a>].</p>
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<p>The charge transfer process between ZnO and MIL-53Al and the degradation routes of AMX [<a href="#B38-ijms-25-09575" class="html-bibr">38</a>]. AMX molecule has Red: Oxygen, Blue: Nitrogen, Yellow: Sulfur, White: Hydrogen, Black: Carbon.</p>
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<p>Recyclability results of AMX in five runs using 0.6 g/L of MIL-53(Al)/ZnO catalyst at pH 7.0, 50 mg/L of AMX, and irradiation time of 60 min [<a href="#B38-ijms-25-09575" class="html-bibr">38</a>].</p>
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<p>Kinetics plots of AMX degradation at (<b>A</b>) pH 4.0, (<b>B</b>) pH 5.5, and (<b>C</b>) pH 7.0 [<a href="#B39-ijms-25-09575" class="html-bibr">39</a>].</p>
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<p>AMX degradation under simulated sunlight and in the dark using inorganic salts: (<b>A</b>) NaCl; (<b>B</b>) CaCl<sub>2</sub>; (<b>C</b>) NaNO<sub>3</sub>; (<b>D</b>) Na<sub>2</sub>HPO<sub>4</sub>; (<b>E</b>) FeCl<sub>3</sub>; and (<b>F</b>) humic acids [<a href="#B39-ijms-25-09575" class="html-bibr">39</a>].</p>
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<p>SEM images of (<b>a</b>) Cu<sub>2</sub>O and (<b>b</b>) Mn-doped Cu<sub>2</sub>O [<a href="#B54-ijms-25-09575" class="html-bibr">54</a>].</p>
Full article ">Figure 22
<p>Effect of pH on photocatalytic degradation of 15 mg/L AMX using 1 g/L of Mn-doped Cu<sub>2</sub>O catalyst [<a href="#B54-ijms-25-09575" class="html-bibr">54</a>].</p>
Full article ">Figure 23
<p>Effect of initial concentration of AMX on photocatalytic degradation using 1 g/L Mn-doped Cu<sub>2</sub>O catalyst at pH 9 [<a href="#B54-ijms-25-09575" class="html-bibr">54</a>].</p>
Full article ">Figure 24
<p>Effect of Mn-doped Cu<sub>2</sub>O catalyst dose on photocatalytic degradation of 15 mg/L AMX at pH 8 [<a href="#B54-ijms-25-09575" class="html-bibr">54</a>].</p>
Full article ">Figure 25
<p>Photodegradation of AMX using Cu<sub>2</sub>O and Mn-doped Cu<sub>2</sub>O under the optimal conditions of 15 mg/L of AMX and 1 g/L of catalyst at pH 9 [<a href="#B54-ijms-25-09575" class="html-bibr">54</a>].</p>
Full article ">Figure 26
<p>Photodegradation of AMX using (<b>a</b>) Ba(Ti<sub>0</sub>.<sub>950</sub>Sc<sub>0</sub>.<sub>025</sub>Nb<sub>0</sub>.<sub>025</sub>)O<sub>3</sub> and (<b>b</b>) the spectra showing degradation with irradiation time [<a href="#B57-ijms-25-09575" class="html-bibr">57</a>].</p>
Full article ">
18 pages, 5732 KiB  
Article
Highly Efficient Electrospun Silver Decorated Graphene Oxide Nanocomposites on Poly(vinylidene fluoride) (PVDF@GO-Ag) Hybrid Membrane for Reduction of 4-Nitrophenol
by Xiaoben Yang, Zhen He, Lei Jin, Huiyang Chen, Qianglin Li, Ling Wu, Zhenghong Huang and Mingxi Wang
Molecules 2024, 29(16), 3930; https://doi.org/10.3390/molecules29163930 - 20 Aug 2024
Viewed by 492
Abstract
Graphene oxide-silver poly(vinylidene fluoride) membranes (PVDF@GO-Ag) were successfully synthesized by the electrospinning method, which exhibited a high catalytic activity using the hydrogenation of 4-nitrophenol (4-NP) as a model reaction in a batch reaction study. The hybrid membranes doped with 1 wt% GO and [...] Read more.
Graphene oxide-silver poly(vinylidene fluoride) membranes (PVDF@GO-Ag) were successfully synthesized by the electrospinning method, which exhibited a high catalytic activity using the hydrogenation of 4-nitrophenol (4-NP) as a model reaction in a batch reaction study. The hybrid membranes doped with 1 wt% GO and 2 wt% Ag (PVDF-1-2) exhibited the most desired performance for the catalytic reduction of 4-NP. Importantly, PVDF-1-2 exhibited excellent cycling stability in 10 catalytic cycle tests and was highly amenable to separation. This property effectively addresses the significant challenges associated with the practical application of nanocatalysts. Furthermore, density-functional theory (DFT) calculations have demonstrated that the GO-Ag nanocomposites exhibit the strongest adsorption capacity for 4-NP when a specific ratio of GO and Ag is achieved, accompanied by the loading of Ag nanoclusters onto GO. Additionally, the study demonstrated that an increase in temperature significantly accelerated the reaction rate, in line with the van’t Hoff rule. This study provides an effective and environmentally friendly solution for the treatment of 4-NP in wastewater. Full article
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Graphical abstract

Graphical abstract
Full article ">Figure 1
<p>SEM images of (<b>a</b>,<b>a’</b>) PVDF, (<b>b</b>,<b>b’</b>) PVDF-0-2, and (<b>c</b>,<b>c’</b>) PVDF-1-2 fibrous membranes.</p>
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<p>(<b>a</b>) EDS analysis of PVDF-1-2; (<b>b</b>) FTIR spectra of PVDF, PVDF-0-2, and PVDF-1-2. (<b>c</b>) Water contact angle test of the electrospun pristine and hybrid PVDF−based fibrous membranes.</p>
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<p>(<b>a</b>) XPS survey spectra; (<b>b</b>) high−resolution C 1s and (<b>c</b>) Ag 3d spectra of PVDF-1-2 fibrous membrane; (<b>d</b>) Raman spectra of pristine PVDF and PVDF−based hybrid membranes.</p>
Full article ">Figure 3 Cont.
<p>(<b>a</b>) XPS survey spectra; (<b>b</b>) high−resolution C 1s and (<b>c</b>) Ag 3d spectra of PVDF-1-2 fibrous membrane; (<b>d</b>) Raman spectra of pristine PVDF and PVDF−based hybrid membranes.</p>
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<p>UV-Vis spectra of the reduction of 4-NP catalyzed by (<b>a</b>) PVDF and (<b>b</b>) PVDF-1-2. Reaction conditions: weight of membrane = 40 mg; [4-NP] = 0.144 mM; [NaBH<sub>4</sub>] = 0.127 M; volume of solution: 50 mL; room temperature; (<b>c</b>) conversion ratio of 4-NP under different initial amounts of 4-NP (20, 30, 40, 50, 60 mL) catalyzed by PVDF-1-2.</p>
Full article ">Figure 5
<p>(<b>a</b>,<b>b</b>) Pseudo-first-order kinetic fitting graphs of catalytic reduction of 4-NP by PVDF-based hybrid membranes; (<b>c</b>) comparison of K<sub>app</sub> for PVDF-based hybrid membranes. Reaction conditions: weight of membrane = 40 mg; [4-NP] = 0.144 mM; [NaBH<sub>4</sub>] = 0.127 M; volume of solution: 50 mL; room temperature.</p>
Full article ">Figure 6
<p>(<b>a</b>–<b>d</b>) Pseudo-first-order kinetic fitting graphs of catalytic reduction of 4-NP by PVDF composites membrane at the different temperatures. (<b>e</b>) Comparison of K<sub>app</sub> for PVDF composites membrane at different temperature; (<b>f</b>) catalytic reduction of 4-NP by PVDF-1-2 in 10 cycles.</p>
Full article ">Figure 7
<p>Top and side views of optimized structures. (<b>a</b>) GO; (<b>b</b>) Ag-B; (<b>c</b>) GO-Ag; (<b>d</b>) GO-Ag-GO.</p>
Full article ">Figure 8
<p>The optimized structures and corresponding adsorption energy for adsorption of 4-NP- on (<b>a</b>) GO; (<b>b</b>) Ag-B; (<b>c</b>) GO-Ag; (<b>d</b>) GO-Ag-GO.</p>
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<p>Possible catalytic mechanism for the reduction of 4-NP to 4-AP over PVDF@GO-Ag using NaBH<sub>4</sub> as hydrogen donor in aqueous solution.</p>
Full article ">Scheme 1
<p>The synthesis mechanism of nanocomposites GO-Ag and PVDF@GO-Ag hybrid membranes.</p>
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17 pages, 4583 KiB  
Article
Biosynthesis of Polyhydroalkanoates Doped with Silver Nanoparticles Using Pseudomonas putida and Pseudomonas aeruginosa for Antibacterial Polymer Applications
by Carmen Liliana Cruz-Romero, Abraham Ulises Chávez-Ramírez, Cyntia R. Flores-Juárez, Noé Arjona, Alejandra Álvarez-López, Laura del Bosque Plata, Vanessa Vallejo-Becerra and Juan de Dios Galindo-de-la-Rosa
Int. J. Mol. Sci. 2024, 25(16), 8996; https://doi.org/10.3390/ijms25168996 - 19 Aug 2024
Viewed by 450
Abstract
In this study, the biosynthesis of polyhydroxyalkanoates (PHAs) was carried out using Pseudomonas putida and Pseudomonas aeruginosa. These PHAs were produced using reagent-grade glycerol and crude glycerol as the carbon sources. The objective was to compare the production of PHAs and to [...] Read more.
In this study, the biosynthesis of polyhydroxyalkanoates (PHAs) was carried out using Pseudomonas putida and Pseudomonas aeruginosa. These PHAs were produced using reagent-grade glycerol and crude glycerol as the carbon sources. The objective was to compare the production of PHAs and to functionalize these polymers with silver nanoparticles to provide antibacterial properties for potential biomedical applications. The findings from the physical and chemical analyses confirmed the successful synthesis and extraction of PHAs, achieving comparable yields using both crude glycerol and reagent-grade glycerol as carbon sources across both strains. Approximately 16% higher PHAs production was obtained using Pseudomonas putida compared to Pseudomonas aeruginosa, and no significant difference was observed in the production rate of PHAs between the two carbon sources used, which means that crude glycerol could be utilized even though it has more impurities. Notably, PHAs functionalized with silver nanoparticles showed improved antibacterial effectiveness, especially those derived from reagent-grade glycerol and the Pseudomonas aeruginosa strain. Full article
(This article belongs to the Special Issue Polymer Materials for Application in Biomedical Fields)
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Figure 1
<p>The bacterial growth rate of strains <span class="html-italic">Pseudomonas aeruginosa</span> (<b>A</b>,<b>B</b>) and <span class="html-italic">Pseudomonas putida</span> (<b>C</b>,<b>D</b>) was measured in a basal medium of minimal salts modified with reagent-grade glycerol (<b>A</b>,<b>C</b>) and crude glycerol (<b>B</b>,<b>D</b>) as the sole carbon source.</p>
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<p>Substrate consumption rate and PHAs production. Substrate consumption rate in black, glycerol (<b>A</b>,<b>C</b>), crude glycerol (<b>B</b>,<b>D</b>), and biopolymer production in blue of the strains <span class="html-italic">Pseudomonas aeruginosa</span> (<b>A</b>,<b>B</b>) and <span class="html-italic">Pseudomonas putida</span> (<b>C</b>,<b>D</b>).</p>
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<p>Thermogravimetric analysis and differential thermal analysis for the PHA obtained from <span class="html-italic">Pseudomonas aeruginosa</span> strain. TGA for <span class="html-italic">Pseudomonas aeruginosa</span> (<b>A</b>,<b>B</b>) <span class="html-italic">Pseudomonas putida</span> (<b>B</b>); (<b>C</b>) DSC heating curves for the PHAs obtained.</p>
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<p>(<b>A</b>) UV-vis absorption spectrum of silver nanoparticles; (<b>B</b>) Intensity-based particle size distribution of an aqueous suspension of silver nanoparticles obtained from DLS analysis; (<b>C</b>) measure- ments as a function of pH for silver nanoparticles suspended in water and acidified with hydrochloric acid solutions.</p>
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<p>FTIR analysis of PHAs from <span class="html-italic">Pseudomonas aeruginosa</span> using (<b>A</b>) reagent-grade glycerol and (<b>B</b>) crude glycerol.</p>
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<p>FTIR analysis of PHAs from <span class="html-italic">Pseudomonas putida</span> using (<b>A</b>) reagent-grade glycerol and (<b>B</b>) crude glycerol.</p>
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<p>Scanning electron micrographs showing the morphology of films formed from <span class="html-italic">Pseudomonas aeuriginosa</span> with reagent-grade glycerol. The control films without silver nanoparticles (<b>A</b>) and the films with silver nanoparticles (<b>B</b>).</p>
Full article ">Figure 8
<p>Scanning electron micrographs showing the morphology of films formed from <span class="html-italic">Pseudomonas putida</span> with reagent-grade glycerol. The control films without silver nanoparticles (<b>A</b>) and the films with silver nanoparticles (<b>B</b>).</p>
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<p>Antibacterial inhibition zone of the discs impregnated with PHAs-silver nanoparticles produced with the <span class="html-italic">Pseudomonas aureginosa</span> strain, with two different concentrations of silver nanoparticles: 0.05 mg/kg (<b>A</b>,<b>C</b>) and 0.5 mg/kg (<b>B</b>,<b>D</b>). Figures (<b>A</b>,<b>B</b>) correspond to the PHAs produced from reagent-grade glycerol, while figures (<b>C,D</b>), the PHAs formed with crude glycerol.</p>
Full article ">Figure 10
<p>Antibacterial inhibition zone of the discs impregnated with PHAs-silver nanoparticles produced with the <span class="html-italic">Pseudomonas putida</span> strain, with two different concentrations of silver nanoparticles, 0.05 mg/kg (<b>A</b>,<b>C</b>) and 0.5 mg/kg (<b>B</b>,<b>D</b>). Figures (<b>A</b>,<b>B</b>) correspond to the PHAs produced from reagent-grade glycerol, while figures (<b>C</b>,<b>D</b>), the PHAs formed with crude glycerol.</p>
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13 pages, 11109 KiB  
Article
A Flexible Wearable Strain Sensor Based on Nano-Silver-Modified Laser-Induced Graphene for Monitoring Hand Movements
by Mian Zhong, Yao Zou, Hongyun Fan, Shichen Li, Yilin Zhao, Bin Li, Bo Li, Yong Jiang, Xiaoqing Xing, Jiaqing Shen and Chao Zhou
Micromachines 2024, 15(8), 989; https://doi.org/10.3390/mi15080989 - 31 Jul 2024
Viewed by 560
Abstract
The advancement in performance in the domain of flexible wearable strain sensors has become increasingly significant due to extensive research on laser-induced graphene (LIG). An innovative doping modification technique is required owing to the limited progress achieved by adjusting the laser parameters to [...] Read more.
The advancement in performance in the domain of flexible wearable strain sensors has become increasingly significant due to extensive research on laser-induced graphene (LIG). An innovative doping modification technique is required owing to the limited progress achieved by adjusting the laser parameters to enhance the LIG’s performance. By pre-treating with AgNO3, we successfully manufactured LIG with a uniform dispersion of silver nanoparticles across its surface. The experimental results for the flexible strain sensor exhibit exceptional characteristics, including low resistance (183.4 Ω), high sensitivity (426.8), a response time of approximately 150 ms, and a relaxation time of about 200 ms. Moreover, this sensor demonstrates excellent stability under various tensile strains and remarkable repeatability during cyclic tests lasting up to 8000 s. Additionally, this technique yields favorable results in finger bending and hand back stretching experiments, holding significant reference value for preserving the inherent characteristics of LIG preparation in a single-step and in situ manner. Full article
(This article belongs to the Special Issue Flexible and Wearable Sensors, 3rd Edition)
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Figure 1
<p>Experimental process of LIG.</p>
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<p>SEM detection of Ag<sub>-x</sub>/LIG. (<b>a</b>) Ag<sub>-0.00</sub>/LIG, (<b>b</b>) Ag<sub>-0.01</sub>/LIG, (<b>c</b>) Ag<sub>-0.03</sub>/LIG, (<b>d</b>) Ag<sub>-0.05</sub>/LIG.</p>
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<p>SEM and EDS detection of Ag<sub>-0.03</sub>/LIG. (<b>a</b>) SEM detection, (<b>b</b>–<b>f</b>) full spectrum and partial spectrum of EDS.</p>
Full article ">Figure 4
<p>Characterization of Ag<sub>-x</sub>/LIG. (<b>a</b>) Raman spectra, (<b>b</b>) calculation value of I<sub>D</sub>/I<sub>G</sub> and I<sub>2D</sub>/I<sub>G</sub>, (<b>c</b>) XRD detection, (<b>d</b>) detection of Ag<sub>-0.03</sub>/LIG, (<b>e</b>) XPS detection, (<b>f</b>) element contnt percentage, (<b>g</b>) C1s sub–peak and fitting, (<b>h</b>) Ag3d sub–peak and fitting, (<b>i</b>) resistance of Ag<sub>-x</sub>/LIG.</p>
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<p>Tensile performance tests of the flexible wearable strain sensor. (<b>a</b>) Tensile strain and reltive resistance tests, (<b>b</b>) tensile strain and relative resistance change test of Ag<sub>-0.03</sub>/LIG–based flexible wearable strain sensor, (<b>c</b>) sensitivity comparison of four flexible wearable strain sensors, (<b>d</b>) senstivity comparison of Ag<sub>-0.03</sub>/LIG–based flexible wearable strain sensors with other materials or processes [<a href="#B17-micromachines-15-00989" class="html-bibr">17</a>,<a href="#B31-micromachines-15-00989" class="html-bibr">31</a>,<a href="#B32-micromachines-15-00989" class="html-bibr">32</a>,<a href="#B33-micromachines-15-00989" class="html-bibr">33</a>,<a href="#B34-micromachines-15-00989" class="html-bibr">34</a>,<a href="#B35-micromachines-15-00989" class="html-bibr">35</a>,<a href="#B36-micromachines-15-00989" class="html-bibr">36</a>,<a href="#B37-micromachines-15-00989" class="html-bibr">37</a>,<a href="#B38-micromachines-15-00989" class="html-bibr">38</a>], (<b>e</b>) stability testing at different tensile lengths, (<b>f</b>) time response testing, (<b>g</b>) cyclic repeatability testing.</p>
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<p>Changes in relative resistance of flexible wearable strain sensors under different tensile forces. (<b>a</b>) Testing the bending condition of the flexible strain sensor in the middle of the hinge, (<b>b</b>) the relative resistance change during the bending process of the flexible strain sensor in the hinge, (<b>c</b>) schematic diagram of finger bending angle, (<b>d</b>) testing the relative resistance changes in flexible strain sensors during finger bending at different angles, (<b>e</b>) the relative resistance change in the flexible strain sensor during the use of the grip strength meter in the test hand.</p>
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<p>Thermal performance test and temperature change curve of LIG-based and Ag<sub>-0.03</sub>/LIG–based flexible wearable strain sensor. (<b>a</b>) Infrared thermal performance test of LIG, (<b>b</b>) temperature change curve during the electric heating performance test of LIG, (<b>c</b>) infrared thermal performance test of Ag<sub>-0.03</sub>/LIG, (<b>d</b>) temperature-change curve during the electric heating performance test of Ag<sub>-0.03</sub>/LIG.</p>
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21 pages, 6973 KiB  
Article
BiVO4-Based Photocatalysts for the Degradation of Antibiotics in Wastewater: Calcination Role after Solvothermal Synthesis
by Jhon Mauricio Aguirre-Cortes, Adriana Isabel Moral-Rodríguez, Esther Bailón-García, Francisco Carrasco-Marín and Agustín Francisco Pérez-Cadenas
Catalysts 2024, 14(8), 474; https://doi.org/10.3390/catal14080474 - 25 Jul 2024
Viewed by 669
Abstract
BiVO4 is an important n-type semiconductor used in photocatalysis due to its high capacity to absorb solar light in the 400–700 nm range, abundance, high chemical stability, non-toxicity, and low cost. However, research on physicochemical modifications to increase its catalytic activity via [...] Read more.
BiVO4 is an important n-type semiconductor used in photocatalysis due to its high capacity to absorb solar light in the 400–700 nm range, abundance, high chemical stability, non-toxicity, and low cost. However, research on physicochemical modifications to increase its catalytic activity via simple procedures is limited. In this work, the influence of different synthesis parameters, such as calcination temperatures or silver doping, on the structural and physicochemical characteristic of the BiVO4-based photocatalysts and their photocatalytic performance in degrading sulfamethoxazole from aqueous solution under blue-LED irradiation was evaluated. BiVO4-based photocatalysts were synthesized using a solvothermal method. The monoclinic phase (m-s) was successfully kept stable even after the thermal treatments at 300, 450, and 600 °C and the corresponding silver doping. The low bandgap of 2.40 eV and the average particle size of 18 nm of the BiVO4 catalyst treated at 300 °C seems to be the key. Afte doping, Ag/BiVO4 photocatalyst treated at the optimal found calcination temperature (300 °C) showed the best photocatalytic behavior. Full article
(This article belongs to the Special Issue Featured Papers in “Environmental Catalysis” Section)
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<p>Photographs of undoped BiV/T (T = 80, 300, 450, and 600 °C) photocatalyst.</p>
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<p>Photodegradation results for SMX degradation after 540 min of irradiation using undoped BiV/T (T = 80, 300, 450, and 600 °C) photocatalysts as a function of calcination temperature. The optimal temperature seems to be 335 °C.</p>
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<p>XRD pattern (<b>a</b>) of undoped BiV/T (T = 80, 300, 450, and 600 °C) and doped Ag/BiV/T (T = 80 and 300 °C) photocatalysts. (<b>b</b>) Enlargement of the 2θ degree area representing the (<span class="html-italic">121</span>) and (<span class="html-italic">040</span>) crystalline planes of (m-s) BiVO<sub>4</sub>, 7.13 and 9.37.</p>
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<p>Correlation of the intensity ratio of I(121)/I(010) and I(040)/I(110) in the diffraction patterns of (<b>a</b>) undoped BiV/T (T = 80, 300, 450, and 600 °C) and (<b>b</b>) doped Ag/BiV/T (T = 80 and 300 °C) photocatalyst with synthesis temperature.</p>
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<p>N<sub>2</sub> adsorption–desorption isotherms of undoped BiV/T (T = 80 and 300 °C) photocatalysts.</p>
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<p>(<b>a</b>) UV-Vis absorbance spectra, (<b>b</b>) E<sub>g</sub> calculations of undoped BiV/T (T = 80, 300, 450 and 600 °C) and doped Ag/BiV/T (T = 80 and 300 °C) photocatalysts.</p>
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<p>SEM images of undoped BiV/T (T = (<b>a</b>,<b>b</b>) 80, (<b>c</b>,<b>d</b>) 300, (<b>e</b>,<b>f</b>) 450, and (<b>g</b>,<b>h</b>) 600 °C).</p>
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<p>HRTEM analysis of sample Ag/BiV/300. (<b>a</b>) single particle at 36,000× magnification, (<b>b</b>,<b>c</b>) lattice fringes of BiVO<sub>4</sub> at 105,000× magnification, (<b>d</b>) diffraction points of BiVO<sub>4</sub>, (<b>e</b>–<b>h</b>) EDX-mapping.</p>
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<p>XPS spectra of undoped BiV/T (T = 80, 300, 450, and 600 °C) photocatalysts (<b>a</b>) C<sub>1s</sub>, (<b>b</b>) Bi<sub>4f</sub>, (<b>c</b>) V<sub>2p</sub>, and (<b>d</b>) O<sub>1s</sub>.</p>
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<p>XPS spectra of silver-doped Ag/BiV/T (T = 80 and 300 °C) photocatalyst (<b>a</b>) C<sub>1s</sub>, (<b>b</b>) Bi<sub>4f</sub>, (<b>c</b>) V<sub>2p</sub>, (<b>d</b>) O<sub>1s</sub>, and (<b>e</b>) Ag<sub>3d5/2</sub>.</p>
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<p>Photodegradation results for SMX degradation using undoped BiV/T (T = 80, 300, 450, and 600 °C) and doped Ag/BiV/T (T = 80 and 300 °C) photocatalysts (dots) under blue-LED irradiation. The best-fit LHHW mathematical models (continuous color lines) are shown to compare the theoretical and experimental trends.</p>
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<p>Schematic representation of steps for solvothermal synthesis of BiVO<sub>4</sub> photocatalysts.</p>
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<p>Schematic photodegradation experiment using the homemade slurry batch LED reactor. (<b>a</b>) Schematic representation of the reaction, (<b>b</b>) box batch reactor containing 5 × 10 blue-LED bulbs and fans to promote cooling, (<b>c</b>) 250 cm3 borosilicate glass reactor containing slurry photocatalyst, and (<b>d</b>) batch reactor dimensions.</p>
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17 pages, 9947 KiB  
Article
Combined Electrochemical Deposition and Photo-Reduction to Fabricate SERS-Active Silver Substrates: Characterization and Application for Malachite Green Detection in Aquaculture Water
by Yu-Xuan Li, Yi-Ting Chen, Cheng-Tse Chang, Chao Yi (Anso) Ting, Yaumalika Arta, Mei-Yao Wu, Tsunghsueh Wu, Yu-Shen Lin and Yang-Wei Lin
Nanomaterials 2024, 14(14), 1226; https://doi.org/10.3390/nano14141226 - 19 Jul 2024
Viewed by 587
Abstract
This research introduces a novel approach using silver (Ag) nanostructures generated through electrochemical deposition and photo-reduction of Ag on fluorine-doped tin oxide glass substrates (denoted as X-Ag-AgyFTO, where ‘X’ and ‘y’ represent the type of light source and number of deposited [...] Read more.
This research introduces a novel approach using silver (Ag) nanostructures generated through electrochemical deposition and photo-reduction of Ag on fluorine-doped tin oxide glass substrates (denoted as X-Ag-AgyFTO, where ‘X’ and ‘y’ represent the type of light source and number of deposited cycles, respectively) for surface-enhanced Raman spectroscopy (SERS). This study used malachite green (MG) as a Raman probe to evaluate the enhancement factors (EFs) in SERS-active substrates under varied fabrication conditions. For the substrates produced via electrochemical deposition, we determined a Raman EF of 6.15 × 104 for the Ag2FTO substrate. In photo-reduction, the impact of reductant concentration, light source, and light exposure duration were examined on X-Ag nanoparticle formation to achieve superior Raman EFs. Under optimal conditions (9.0 mM sodium citrate, 460 nm blue-LED at 10 W for 90 min), the combination of blue-LED-reduced Ag (B-Ag) and an Ag2FTO substrate (denoted as B-Ag-Ag2FTO) exhibited the best Raman EF of 2.79 × 105. This substrate enabled MG detection within a linear range of 0.1 to 1.0 µM (R2 = 0.98) and a detection limit of 0.02 µM. Additionally, the spiked recoveries in aquaculture water samples were between 90.0% and 110.0%, with relative standard deviations between 3.9% and 6.3%, indicating the substrate’s potential for fungicide detection in aquaculture. Full article
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<p>(<b>A</b>) SEM image, (<b>B</b>) EDS spectrum, and (<b>C</b>) elemental mapping of Ag<sub>1</sub>FTO substrate.</p>
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<p>(<b>A</b>) SEM image, (<b>B</b>) EDS spectrum, and (<b>C</b>) elemental mapping of Ag<sub>2</sub>FTO substrate.</p>
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<p>(<b>A</b>) SERS spectra of 1.0 μM MG on different substrates: FTO (black spectrum), Ag<sub>1</sub>FTO (red spectrum), Ag<sub>2</sub>FTO (blue spectrum), and Ag<sub>3</sub>FTO (pink spectrum). (<b>B</b>) SEM images and EDS-mapping for Ag<sub>1</sub>FTO, Ag<sub>2</sub>FTO, and Ag<sub>3</sub>FTO substrates.</p>
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<p>Raman signals of MG (10.0 μM) at 1614 cm<sup>−1</sup> for (<b>A</b>) Ag<sub>1</sub>FTO and (<b>B</b>) Ag<sub>2</sub>FTO substrates across various electroplating voltages and deposition times.</p>
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<p>SERS spectra (Inset: Raman signal at 1614 cm<sup>−1</sup>) for varying concentrations of MG using (<b>A</b>) Ag<sub>1</sub>FTO and (<b>B</b>) Ag<sub>2</sub>FTO substrates.</p>
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<p>UV–Vis spectra of B-Ag solutions prepared at different concentrations of sodium citrate.</p>
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<p>UV–Vis spectra of X-Ag solutions prepared with varying irradiation times: (<b>A</b>) 30, (<b>B</b>) 60, (<b>C</b>) 90, (<b>D</b>) 120, and (<b>E</b>) 150 min. Inset: photographic images of respective X-Ag solutions.</p>
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<p>TEM images of (<b>A</b>) B-Ag, (<b>B</b>) UV-Ag, and (<b>C</b>) W-Ag.</p>
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<p>(<b>A</b>) SERS spectra and (<b>B</b>) Raman signals of MG (1.0 μM) at 1614 cm<sup>−1</sup> on B-Ag/Ag<sub>1</sub>FTO substrates, where B-Ag was prepared at different concentrations of sodium citrate.</p>
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<p>Raman signals of 1.0 μM MG at 1614 cm<sup>−1</sup> on X-Ag/Ag<sub>1</sub>FTO substrate, where X-Ag was prepared using different light sources.</p>
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<p>SERS spectra (Inset: Raman signal at 1614 cm<sup>−1</sup>) of MG at different concentrations, analyzed using (<b>A</b>) B-Ag/Ag<sub>1</sub>FTO and (<b>B</b>) B-Ag/Ag<sub>2</sub>FTO substrates.</p>
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<p>Signal reproducibility of (<b>A</b>) different days in B-Ag-Ag<sub>2</sub>FTO substrate and (<b>B</b>) different fabricated batches of B-Ag-Ag<sub>2</sub>FTO substrates.</p>
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<p>(<b>A</b>) Electroplating system setup, (<b>B</b>) light irradiation system for prepared X-Ag, and (<b>C</b>) schematic illustration of nanoparticle-on-mirror (NPoM) fabrication for SERS analysis.</p>
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15 pages, 3558 KiB  
Article
Polymer-Based Hydroxyapatite–Silver Composite Resin with Enhanced Antibacterial Activity for Dental Applications
by Jesús Alberto Garibay-Alvarado, Diana Juana Garcia-Zamarron, Pamela Nair Silva-Holguín, Alejandro Donohue-Cornejo, Juan Carlos Cuevas-González, León Francisco Espinosa-Cristóbal, Álvaro de Jesús Ruíz-Baltazar and Simón Yobanny Reyes-López
Polymers 2024, 16(14), 2017; https://doi.org/10.3390/polym16142017 - 15 Jul 2024
Viewed by 807
Abstract
The primary objective of this investigation was to synthesize a resin incorporating nanoparticles of hydroxyapatite and silver (HA-NpsAg) to enhance biocompatibility and antimicrobial efficacy, thereby facilitating potential implementation within the dental industry. These enhancements aim to ensure reliable, durable, functional, and aesthetically pleasing [...] Read more.
The primary objective of this investigation was to synthesize a resin incorporating nanoparticles of hydroxyapatite and silver (HA-NpsAg) to enhance biocompatibility and antimicrobial efficacy, thereby facilitating potential implementation within the dental industry. These enhancements aim to ensure reliable, durable, functional, and aesthetically pleasing restorations while concurrently reducing susceptibility to bacterial colonization within the oral cavity. Hydroxyapatite powders were prepared using the sol–gel method and doped with silver nanoparticles obtained by chemical reduction. The crystalline amorphous calcium phosphate powder had a particle size of 279 nm, and the silver nanoparticles had an average diameter of 26.5 nm. Resin spheres containing HA-NpsAg (RHN) were then synthesized at two concentrations (0.5% and 1%) by dissolving the initial monomer mixture in tetrahydrofuran. Subsequent antimicrobial evaluations were conducted via agar diffusion and turbidimetry, employing three strains of Gram-negative bacteria (E. coli, K. oxytoca, and P. aeruginosa) and three strains of Gram-positive bacteria (S. mutans, S. aureus, and B. subtilis). The findings revealed that P. aeruginosa exhibited maximum susceptibility to RHN powder at a concentration of 0.5%, while RHN powder at 1% concentration demonstrated maximal inhibition against S. aureus and S. mutans. Overall, our study highlights the successful synthesis of a dental resin with hydroxyapatite and silver nanoparticles, exhibiting bactericidal properties at low silver concentrations. These findings hold promise for enhancing dental materials with improved antimicrobial efficacy and clinical performance. Full article
(This article belongs to the Topic Antimicrobial Agents and Nanomaterials)
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<p>Characterization of HA powder: (<b>a</b>) IR spectra, (<b>b</b>) Raman spectra, (<b>c</b>) X-ray diffractogram, (<b>d</b>) UV–Vis spectra, (<b>e</b>) STEM micrography with EDX spectra, and (<b>f</b>) DLS size histogram of hydroxyapatite powder.</p>
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<p>(<b>a</b>) Absorption UV–Vis spectra of the silver nanoparticles, (<b>b</b>) silver nanoparticles size histogram, (<b>c</b>) photograph of the nanoparticle solution, (<b>d</b>) and STEM micrography of the nanoparticles.</p>
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<p>UV–Vis spectra of the hydroxyapatite–silver nanoparticles powder at 50 mM.</p>
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<p>ATR-FTIR spectra of the hydroxyapatite and hydroxyapatite–silver nanoparticles powder (0.25 and 0.50 mM).</p>
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<p>IR spectra of composite resin with 0.50 mM of silver (blue), 0.25 mM of silver (red), and with hydroxyapatite (black).</p>
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<p>XRD patterns of the composite resin with hydroxyapatite and silver 0.50 mM (blue), silver 0.25 mM (red), and 0.00 mM (black).</p>
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<p>Box-plot of the inhibition behavior of the HA-AgNPs composite resin over 3 species of Gram-negative and 3 species of Gram-positive bacteria at 8 h. (<b>a</b>) <span class="html-italic">Escherichia coli</span>, (<b>b</b>) <span class="html-italic">Bacillus subtilis</span>, (<b>c</b>) <span class="html-italic">Klebsiella oxytoca</span>, (<b>d</b>) <span class="html-italic">Staphylococcus aureus</span>, (<b>e</b>) <span class="html-italic">Pseudomonas aeruginosa</span> and (<b>f</b>) <span class="html-italic">Streptococcus mutans</span>. (*) The asterisk on the box-plots stands for “significantly different”.</p>
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17 pages, 3123 KiB  
Article
The Difference between Plasmon Excitations in Chemically Heterogeneous Gold and Silver Atomic Clusters
by Fanjin Zeng, Lin Long, Shuyi Wang, Xiong Li, Shaohong Cai and Dongxiang Li
Molecules 2024, 29(14), 3300; https://doi.org/10.3390/molecules29143300 - 12 Jul 2024
Viewed by 591
Abstract
Weak doping can broaden, shift, and quench plasmon peaks in nanoparticles, but the mechanistic intricacies of the diverse responses to doping remain unclear. In this study, we used the time-dependent density functional theory (TD-DFT) to compute the excitation properties of transition-metal Pd- or [...] Read more.
Weak doping can broaden, shift, and quench plasmon peaks in nanoparticles, but the mechanistic intricacies of the diverse responses to doping remain unclear. In this study, we used the time-dependent density functional theory (TD-DFT) to compute the excitation properties of transition-metal Pd- or Pt-doped gold and silver atomic arrays and investigate the evolution characteristics and response mechanisms of their plasmon peaks. The results demonstrated that the Pd or Pt doping of the off-centered 10 × 2 atomic arrays broadened or shifted the plasmon peaks to varying degrees. In particular, for Pd-doped 10 × 2 Au atomic arrays, the broadened plasmon peak significantly blueshifted, whereas a slight red shift was observed for Pt-doped arrays. For the 10 × 2 Ag atomic arrays, Pd doping caused almost no shift in the plasmon peak, whereas Pt doping caused a substantial red shift in the broadened plasmon peak. The analysis revealed that the diversity in these doping responses was related to the energy positions of the d electrons in the gold and silver atomic clusters and the positions of the doping atomic orbitals in the energy bands. The introduction of doping atoms altered the symmetry and gap size of the occupied and unoccupied orbitals, so multiple modes of single-particle transitions were involved in the excitation. An electron transfer analysis indicated a close correlation between excitation energy and the electron transfer of doping atoms. Finally, the differences in the symmetrically centered 11 × 2 doped atomic array were discussed using electron transfer analysis to validate the reliability of this analytical method. These findings elucidate the microscopic mechanisms of the evolution of plasmon peaks in doped atomic clusters and provide new insights into the rational control and application of plasmons in low-dimensional nanostructures. Full article
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<p>Absorption spectra of the (<b>a</b>) 10 × 2 Au:2X atomic array(X = Au, Pd, Pt), and (<b>b</b>) 10 × 2 Ag:2X atomic array(X = Ag, Pd, Pt).</p>
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<p>(<b>a</b>) Orbital energy diagrams of the 10 × 2 Au atomic arrays. (<b>b</b>) Orbital energy diagrams of the 10 × 2 Ag atomic arrays.</p>
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<p>(<b>a</b>) Dividing a pure 10 × 2 Au atomic array into three fragments. (<b>b</b>) Dividing a pure 10 × 2 Ag atomic array into three fragments. (<b>c</b>) Dividing a 10 × 2 Au atomic array with off-center doped into three fragments. (<b>d</b>) Dividing a 10 × 2 Ag atomic array with off-center doped into three fragments.</p>
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<p>(<b>a</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>19</sub> state of the 10 × 2 Au atomic array. (<b>b</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>51</sub> state of the 10 × 2 Au:2Pd atomic array. (<b>c</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>65</sub> state of the 10 × 2 Au:2Pd atomic array. (<b>d</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>15</sub> state of the 10 × 2 Ag atomic array. (<b>e</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>34</sub> state of the 10 × 2 Ag:2Pd atomic array. (<b>f</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>56</sub> state of the 10 × 2 Ag:2Pd atomic array. (<b>g</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>35</sub> state of the 10 × 2 Ag:2Pt atomic array. (<b>h</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>60</sub> state of the 10 × 2 Ag:2Pt atomic array.(“→”or “←” represents the direction of electron transfer.).</p>
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<p>(<b>a</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>19</sub> state of the 10 × 2 Au atomic array. (<b>b</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>51</sub> state of the 10 × 2 Au:2Pd atomic array. (<b>c</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>65</sub> state of the 10 × 2 Au:2Pd atomic array. (<b>d</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>15</sub> state of the 10 × 2 Ag atomic array. (<b>e</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>34</sub> state of the 10 × 2 Ag:2Pd atomic array. (<b>f</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>56</sub> state of the 10 × 2 Ag:2Pd atomic array. (<b>g</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>35</sub> state of the 10 × 2 Ag:2Pt atomic array. (<b>h</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>60</sub> state of the 10 × 2 Ag:2Pt atomic array.(“→”or “←” represents the direction of electron transfer.).</p>
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<p>Absorption spectra of the (<b>a</b>) 10 × 2 Au:2X atomic array (X = Au, Pd, Pt), and (<b>b</b>) 10 × 2 Ag:2X atomic array (X = Ag, Pd, Pt). (employed the CAM-B3LYP functional).</p>
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<p>Absorption spectra of the (<b>a</b>) 11 × 2 Au:2X atomic array (X = Au, Pd, Pt), and (<b>b</b>) 11 × 2 Ag:2X atomic array (X = Ag, Pd, Pt).</p>
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<p>(<b>a)</b> Dividing a pure 11 × 2 Au atomic array into three fragments. (<b>b</b>) Dividing a pure 11 × 2 Ag atomic array into three fragments. (<b>c</b>) Dividing a 11 × 2 Au atomic array with symmetrically center-doped into three fragments. (<b>d</b>) Dividing a 11 × 2 Ag atomic array with symmetrically center-doped into three fragments.</p>
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<p>(<b>a</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>17</sub> state of the 11 × 2 Ag atomic array. (<b>b</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>39</sub> state of the 11 × 2 Au:2Pd atomic array. (<b>c</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>32</sub> state of the 11 × 2 Ag:2Pd atomic array. (<b>d</b>) Net electron transfer from the S<sub>0</sub> state to the S<sub>43</sub> state of the 11 × 2 Ag:2Pt atomic array.(“→”or “←” represents the direction of electron transfer.)</p>
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17 pages, 5559 KiB  
Article
Exploring Enhanced Structural and Dielectric Properties in Ag-Doped Sr(NiNb)0.5O3 Perovskite Ceramic for Advanced Energy Storage
by Faouzia Tayari, Majdi Benamara, Madan Lal, Manel Essid, Priyanka Thakur, Deepak Kumar, S. Soreto Teixeira, M. P. F. Graça and Kais Iben Nassar
Ceramics 2024, 7(3), 958-974; https://doi.org/10.3390/ceramics7030062 - 10 Jul 2024
Cited by 1 | Viewed by 746
Abstract
The ceramic Sr(NiNb)0.5O3, incorporating silver doping in the A site, was synthesized using a sol–gel route and subjected to comprehensive analysis through various experimental techniques. X-ray diffraction data analysis indicates a rhombohedral crystal structure. Scanning electron microscopy (SEM) examination [...] Read more.
The ceramic Sr(NiNb)0.5O3, incorporating silver doping in the A site, was synthesized using a sol–gel route and subjected to comprehensive analysis through various experimental techniques. X-ray diffraction data analysis indicates a rhombohedral crystal structure. Scanning electron microscopy (SEM) examination reveals densely packed grains with minimal surface porosity. A thorough investigation of electrical properties, encompassing dielectric constant, loss tangent, electrical impedance, modulus, conductivity, etc., was conducted across a wide frequency range (103–106 Hz) and temperature range (260–340 K). This analysis provided valuable insights into structure–property relationships and conduction mechanisms. The discussion highlights the significance of interface effects, space charge polarization, and Maxwell–Wagner dielectric relaxation in achieving the material’s high dielectric constant at low frequencies and elevated temperatures. Examination of temperature dependence through Nyquist plots elucidates the contributions of grain behavior to the material’s resistive and capacitive properties. The dielectric permittivity, dissipation of energy, and electrical characteristics like impedance, modulus and conductivity are notably influenced by the frequency of the applied electric field and temperature. Overall, the material exhibits promising potential for industrial applications such as energy storage, given its intriguing properties. Full article
(This article belongs to the Special Issue Advances in Electronic Ceramics)
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<p>Synthesis process of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> perovskite through the sol–gel method. SEM, XRD, and ISC stand for scanning electron microscopy, X-ray diffraction, and impedance spectroscopy complex, respectively.</p>
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<p>XRD pattern of of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic.</p>
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<p>(<b>a</b>) SEM micrograph and (<b>b</b>) EDX compositions of the sample.</p>
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<p>Frequency dependence of (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>ε</mi> </mrow> </semantics></math> and (<b>b</b>) tan δ of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic for various temperatures.</p>
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<p>Frequency dependence of (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>ε</mi> </mrow> </semantics></math> and (<b>b</b>) tan δ of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic for various temperatures.</p>
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<p>Temperature dependence of (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>ε</mi> </mrow> </semantics></math> and (<b>b</b>) tan δ of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic for various frequencies.</p>
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<p>Temperature dependence of (<b>a</b>) <math display="inline"><semantics> <mrow> <mi>ε</mi> </mrow> </semantics></math> and (<b>b</b>) tan δ of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic for various frequencies.</p>
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<p>(<b>a</b>) Variation of real part of impedance (Z′) with frequency measured at different temperatures for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub>. (<b>b</b>) Variation of imaginary part of impedance (Z″) with frequency measured at different temperatures for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub>.</p>
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<p>Nyquist plots for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic at different temperatures.</p>
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<p>(<b>a</b>) Variation of reel part of electrical modulus (M′) with frequency at different temperatures for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic. (<b>b</b>) Variation of imaginary part of electrical modulus (M″) with frequency at different temperatures for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic.</p>
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<p>Arrhenius plot of Ln(F<sub>max</sub>) vs. (1000/T) for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> perovskite.</p>
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<p>Variation of AC conductivity of (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> ceramic with frequency at different temperatures.</p>
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<p>Variation of Ln(σ<sub>dc</sub>) as a function of (1000/T) for (Sr<sub>0.75</sub>Ag<sub>0.25</sub>)(NiNb)<sub>0.5</sub>O<sub>3</sub> perovskite.</p>
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13 pages, 5276 KiB  
Article
Flexible Resistive Gas Sensor Based on Molybdenum Disulfide-Modified Polypyrrole for Trace NO2 Detection
by Kuo Zhao, Yunbo Shi, Mingrui Cui, Bolun Tang, Canda Zheng, Qinglong Chen and Yuhan Hu
Polymers 2024, 16(13), 1940; https://doi.org/10.3390/polym16131940 - 7 Jul 2024
Viewed by 778
Abstract
High sensitivity and selectivity and short response and recovery times are important for practical conductive polymer gas sensors. However, poor stability, poor selectivity, and long response times significantly limit the applicability of single-phase conducting polymers, such as polypyrrole (PPy). In this study, PPy/MoS [...] Read more.
High sensitivity and selectivity and short response and recovery times are important for practical conductive polymer gas sensors. However, poor stability, poor selectivity, and long response times significantly limit the applicability of single-phase conducting polymers, such as polypyrrole (PPy). In this study, PPy/MoS2 composite films were prepared via chemical polymerization and mechanical blending, and flexible thin-film resistive NO2 sensors consisting of copper heating, fluorene polyester insulating, and PPy/MoS2 sensing layers with a silver fork finger electrode were fabricated on a flexible polyimide substrate using a flexible electronic printer. The PPy/MoS2 composite films were characterized using X-ray diffraction, Fourier-transform infrared spectroscopy, and field-emission scanning electron microscopy. A home-built gas sensing test platform was built to determine the resistance changes in the composite thin-film sensor with temperature and gas concentration. The PPy/MoS2 sensor exhibited better sensitivity, selectivity, and stability than a pure PPy sensor. Its response to 50 ppm NO2 was 38% at 150 °C, i.e., 26% higher than that of the pure PPy sensor, and its selectivity and stability were also higher. The greater sensitivity was attributed to p–n heterojunction formation after MoS2 doping and more gas adsorption sites. Thus, PPy/MoS2 composite film sensors have good application prospects. Full article
(This article belongs to the Special Issue Polymers for Biosensors and Detection)
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<p>Schematic of PPy/MoS<sub>2</sub> composite preparation procedure.</p>
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<p>Schematics of (<b>a</b>) overall sensor structure, (<b>b</b>) multilayer sensor structure, and (<b>c</b>) gas sensing test platform.</p>
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<p>SEM images of (<b>a</b>,<b>b</b>) the PPy and (<b>c</b>–<b>f</b>) the PPy/MoS<sub>2</sub> composite, and (<b>f1</b>–<b>f4</b>) elemental distribution maps of the view of the composite shown in the SEM image in panel (<b>f</b>).</p>
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<p>(<b>a</b>) XRD patterns and (<b>b</b>) FTIR spectra of pure PPy and PPy/MoS<sub>2</sub> composites with various MoS<sub>2</sub> mass fractions.</p>
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<p>The TG and DTA curves of (<b>a</b>) PPy and (<b>b</b>) the PPy/MoS<sub>2</sub> composite.</p>
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<p>(<b>a</b>) Resistance and (<b>b</b>) sensitivity of sensors based on composites with different MoS<sub>2</sub> contents at 100 ppm NO<sub>2</sub>.</p>
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<p>Comparison of (<b>a</b>) sensitivity and (<b>b</b>) response/recovery times of 10% PPy/MoS<sub>2</sub> sensor at 100 ppm NO<sub>2</sub> and different temperatures.</p>
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<p>The change in resistance with a NO<sub>2</sub> concentration in the range of 1 to 20 ppm at 150 °C for the (<b>a</b>) pure PPy and (<b>b</b>) PPy/MoS<sub>2</sub> 10% sensors.</p>
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<p>(<b>a</b>) Repeatability at 150 °C and 100 ppm NO<sub>2</sub> of PPy/MoS<sub>2</sub> sensor and (<b>b</b>) selectivities of PPy and PPy/MoS<sub>2</sub> sensors for NO<sub>2</sub>.</p>
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<p>The long-term stabilities of the PPy and PPy/MoS<sub>2</sub> sensors.</p>
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<p>(<b>a</b>) A schematic diagram of the mechanism underlying the enhanced performance of the PPy/MoS<sub>2</sub> composite sensor. (<b>b</b>) A schematic energy diagram of the PPy–MoS<sub>2</sub> heterojunction.</p>
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13 pages, 4169 KiB  
Article
Synergistic Enhancement of Electron Dynamics and Optical Properties in Zeolitic Imidazolate Framework-8-Derived Zinc Oxide via Surface Plasmon Resonance Effects of Silver Nanoparticles under UV Irradiation
by Jaewon Lee and Byoung-Nam Park
Materials 2024, 17(13), 3193; https://doi.org/10.3390/ma17133193 - 29 Jun 2024
Viewed by 584
Abstract
This study investigates the surface plasmon resonance (SPR)-induced UV photoresponse of zinc oxide (ZnO) derived from zeolitic imidazolate framework-8 (ZIF-8) to assess the influence of silver nanoparticles (Ag NPs) on the photoresponse behavior of metal–organic framework (MOF)-derived ZnO. The initial synthesis involved a [...] Read more.
This study investigates the surface plasmon resonance (SPR)-induced UV photoresponse of zinc oxide (ZnO) derived from zeolitic imidazolate framework-8 (ZIF-8) to assess the influence of silver nanoparticles (Ag NPs) on the photoresponse behavior of metal–organic framework (MOF)-derived ZnO. The initial synthesis involved a thermal treatment in air to convert ZIF-8 into ZnO. We noted enhanced optical absorption both in the UV and visible spectra with the deposition of Ag NPs onto the ZIF-8-derived ZnO. Additionally, the presence of Ag NPs in the ZnO resulted in a substantial increase in current, even without any light exposure. This increase is attributed to the transfer of electrons from the Ag NPs to the ZnO. Photocurrent measurements under UV illumination revealed that the photocurrent with Ag NPs was significantly higher—by two orders of magnitude—compared with that without Ag NPs. This demonstrates that SPR-induced absorption markedly boosted the photocurrent, although the current rise and decay time constants remained comparable to those observed with ZnO alone. Although Ag NPs contribute electrons to ZnO, creating a “pre-doping” effect that heightens baseline conductivity (even in the absence of light), this does not necessarily alter the recombination dynamics of the photogenerated carriers, as indicated by the similar rise and decay time constants. The electron transfer from Ag to ZnO increases the density of charge carriers but does not significantly influence their recombination. Full article
(This article belongs to the Special Issue Advanced Science and Technology of Nano-Photocatalytic Materials)
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<p>(<b>a</b>) Diagram illustrating the process of synthesizing ZIF-8. (<b>b</b>) SEM image showcasing the produced ZIF-8 crystals.</p>
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<p>X-ray diffraction patterns comparing ZIF-8 before and after thermal annealing to produce ZIF-8-derived ZnO. The red bars represent theoretical XRD peaks.</p>
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<p>SEM comparison images of (<b>a</b>) original ZIF-8 and (<b>b</b>) ZIF-8-derived ZnO.</p>
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<p>Optical absorption spectra of (<b>a</b>) ZIF-8, ZIF-8-derived ZnO, and ZIF-8-derived ZnO with Ag NPs; (<b>b</b>) optical absorption of Ag NPs on a glass substrate. XPS spectra of Ag/ZIF-8-derived ZnO for (<b>c</b>) Zn 2p and (<b>d</b>) Ag 3d.</p>
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<p>Current–voltage characteristics of ZIF-8-derived ZnO with and without Ag NPs, presented on (<b>a</b>) linear and (<b>b</b>) logarithmic scales in the absence of light.</p>
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<p>Current–time response measurements of ZIF-8-derived ZnO (<b>a</b>) without and (<b>b</b>) with Ag NPs under cycles of UV light exposure and non-exposure, with the drain voltage held constant at 0.05 V. (<b>c</b>) Logarithmic comparison of plots (<b>a</b>,<b>b</b>).</p>
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<p>Current–time response measurements of ZIF-8-derived ZnO (<b>a</b>) without and (<b>b</b>) with Ag NPs under cycles of UV light exposure and non-exposure, with the drain voltage held constant at 0.05 V. (<b>c</b>) Logarithmic comparison of plots (<b>a</b>,<b>b</b>).</p>
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<p>Energy band diagrams illustrating the interface between ZIF-8-derived ZnO and Ag both in (<b>a</b>) darkness and (<b>b</b>) under UV light exposure.</p>
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14 pages, 9952 KiB  
Article
Silver-Assisted Chemical Etching for the Fabrication of Porous Silicon N-Doped Nanohollow Carbon Spheres Composite Anodes to Enhance Electrochemical Performance
by Zimu Zhang, Yuqi Zhang, Weixuan Chen, Xiang Zhang, Le Yu and Zisheng Guan
Materials 2024, 17(13), 3189; https://doi.org/10.3390/ma17133189 - 29 Jun 2024
Viewed by 543
Abstract
Silicon (Si) shows great potential as an anode material for lithium-ion batteries. However, it experiences significant expansion in volume as it undergoes the charging and discharging cycles, presenting challenges for practical implementation. Nanostructured Si has emerged as a viable solution to address these [...] Read more.
Silicon (Si) shows great potential as an anode material for lithium-ion batteries. However, it experiences significant expansion in volume as it undergoes the charging and discharging cycles, presenting challenges for practical implementation. Nanostructured Si has emerged as a viable solution to address these challenges. However, it requires a complex preparation process and high costs. In order to explore the above problems, this study devised an innovative approach to create Si/C composite anodes: micron-porous silicon (p-Si) was synthesized at low cost at a lower silver ion concentration, and then porous silicon-coated carbon (p-Si@C) composites were prepared by compositing nanohollow carbon spheres with porous silicon, which had good electrochemical properties. The initial coulombic efficiency of the composite was 76.51%. After undergoing 250 cycles at a current density of 0.2 A·g−1, the composites exhibited a capacity of 1008.84 mAh·g−1. Even when subjected to a current density of 1 A·g−1, the composites sustained a discharge capacity of 485.93 mAh·g−1 even after completing 1000 cycles. The employment of micron-structured p-Si improves cycling stability, which is primarily due to the porous space it provides. This porous structure helps alleviate the mechanical stress caused by volume expansion and prevents Si particles from detaching from the electrodes. The increased surface area facilitates a longer pathway for lithium-ion transport, thereby encouraging a more even distribution of lithium ions and mitigating the localized expansion of Si particles during cycling. Additionally, when Si particles expand, the hollow carbon nanospheres are capable of absorbing the resulting stress, thus preventing the electrode from cracking. The as-prepared p-Si utilizing metal-assisted chemical etching holds promising prospects as an anode material for lithium-ion batteries. Full article
(This article belongs to the Section Energy Materials)
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<p>Schematic illustration of formation procedure of the p-Si, the p-Si@SiO<sub>2</sub> and the p-Si@C composites.</p>
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<p>SEM images of the Si (<b>a</b>), the p-Si (<b>b</b>,<b>c</b>), the p-Si@SiO<sub>2</sub> (<b>d</b>) and the p-Si@C composite (<b>e</b>,<b>f</b>) and the corresponding elemental mapping images of Si (<b>h</b>), C (<b>i</b>), N (<b>j</b>) and O (<b>k</b>) of the p-Si@C (<b>g</b>) composites.</p>
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<p>Low-magnification (<b>a</b>) and high-magnification (<b>b</b>) TEM image of the p-Si@C composites, (<b>c</b>,<b>d</b>) hollow carbon nanospheres and their wall thicknesses.</p>
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<p>N<sub>2</sub> adsorption–desorption isotherms; (<b>a</b>,<b>b</b>) BJH mesopore size distributions of the p-Si.</p>
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<p>(<b>a</b>) XRD patterns of p-Si, Si@C and p-Si@C composites; (<b>b</b>) TG curves of p-Si@C composites; (<b>c</b>) Raman spectra of the Si@C and p-Si@C composites.</p>
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<p>(<b>a</b>) XPS survey of the p-Si@C composites; the high-resolution XPS spectra of (<b>b</b>) C 1 s, (<b>c</b>) N 1 s, and (<b>d</b>) Si 2p of the p-Si@C composites.</p>
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<p>(<b>a</b>) CV tests of the p-Si@C composites for the first five cycles; (<b>b</b>) the charge–discharge curves for the first five cycles, (<b>c</b>) cycling performance at 0.2 A·g<sup>−1</sup> and (<b>d</b>) rate performance at various current densities for the Si@C and the p-Si@C composites; (<b>e</b>) long-term cycle of the p-Si@C composites at 1 A·g<sup>−1</sup>.</p>
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<p>EIS of the p-Si@C composites before charge/discharge cycling.</p>
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<p>The SEM images of Si@C electrode before (<b>a</b>) and after cycles (<b>d</b>) and p-Si@C electrode before (<b>b</b>,<b>c</b>) and after cycles (<b>e</b>,<b>f</b>).</p>
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14 pages, 3659 KiB  
Article
Study on Novel SCR Catalysts for Denitration of High Concentrated Nitrogen Oxides and Their Reaction Mechanisms
by Bo Yu, Xingyu Liu, Shufeng Wu, Heng Yang, Shuran Zhou, Li Yang and Fang Liu
Catalysts 2024, 14(7), 406; https://doi.org/10.3390/catal14070406 - 27 Jun 2024
Viewed by 550
Abstract
With the rapid development of industrialization, the emission of nitrogen oxides (NOx) has become a global environmental issue. Uranium is the primary fuel used in nuclear power generation. However, the production of uranium, typically based on the uranyl nitrate method, usually [...] Read more.
With the rapid development of industrialization, the emission of nitrogen oxides (NOx) has become a global environmental issue. Uranium is the primary fuel used in nuclear power generation. However, the production of uranium, typically based on the uranyl nitrate method, usually generates large amounts of nitrogen oxides, particularly NO2, with concentrations in the exhaust gas exceeding 10,000 ppm. High concentrations of nitrogen dioxide are also produced during silver electrolysis processing and the treatment of waste electrolyte solutions. Traditional V-W/TiO2 NH3-SCR catalysts typically exhibit high catalytic activity at temperatures ranging from 300 to 400 °C, under conditions of low NOx concentrations and high gas hourly space velocity. However, their performance is not satisfying when reducing high concentrations of NO2. This study aims to optimize the traditional V-W/TiO2 catalysts to enhance their catalytic activity under conditions of high NO2 concentrations (10,000 ppm) and a wide temperature range (200–400 °C). On the basis of 3 wt% Mo/TiO2, various loadings of V2O5 were selected, and their catalytic activities were tested. Subsequently, the optimal ratios of active component vanadium and additive molybdenum were explored. Simultaneously, doping with WO3 for modification was selected in the V-Mo/TiO2 catalyst, followed by activity testing under the same conditions. The results show that: the NOx conversion rates of all five catalysts increase with temperature at range of 200–400 °C. Excessive loading of MoO3 decreased the catalytic performance, with 5 wt% being the optimal loading. The addition of WO3 significantly enhanced the low-temperature activity of the catalysts. When the loadings of WO3 and MoO3 were both 3 wt%, the catalyst exhibited the best denitrification performance, achieving a NOx conversion rate of 98.8% at 250 °C. This catalyst demonstrates excellent catalytic activity in reducing very high concentration (10,000 ppm) NO2, at a wider temperature range, expanding the temperature range by 50% compared to conventional SCR catalysts. Characterization techniques including BET, XRD, XPS, H2-TPR, and NH3-TPD were employed to further study the evolution of the catalyst, and the promotional mechanisms are explored. The results revealed that the proportion of chemisorbed oxygen (Oα) increased in the WO3-modified catalyst, exhibiting lower V reduction temperatures, which are favorable for low-temperature denitrification activity. NH3-TPD experiments showed that compared to MoOx species, surface WOx species could provide more acidic sites, resulting in stronger surface acidity of the catalyst. Full article
(This article belongs to the Section Environmental Catalysis)
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<p>NO conversions of NH<sub>3</sub>-SCR over catalysts with different V<sub>2</sub>O<sub>5</sub> doping.</p>
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<p>NO conversions of NH<sub>3</sub>-SCR over catalysts with different MoO<sub>3</sub> and WO<sub>3</sub> doping.</p>
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<p>Pore parameter curves of V<sub>3</sub>Mo<sub>5</sub>/TiO<sub>2</sub> and V<sub>3</sub>W<sub>3</sub>Mo<sub>3</sub>/TiO<sub>2</sub> catalysts: (<b>a</b>) N<sub>2</sub> adsorption-desorption isotherms; (<b>b</b>) pore size distribution.</p>
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<p>XRD patterns of catalysts with different MoO<sub>3</sub>, WO<sub>3</sub> doping.</p>
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<p>NH<sub>3</sub>-TPD curves of V<sub>3</sub>Mo<sub>5</sub>/TiO<sub>2</sub> and V<sub>3</sub>W<sub>3</sub>Mo<sub>3</sub>/TiO<sub>2</sub> catalysts.</p>
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<p>H<sub>2</sub>-TPR curves of V<sub>3</sub>Mo<sub>5</sub>/TiO<sub>2</sub> and V<sub>3</sub>W<sub>3</sub>Mo<sub>3</sub>/TiO<sub>2</sub> catalysts.</p>
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<p>The XPS spectra of catalysts with varying MoO<sub>3</sub> and WO<sub>3</sub> loading amounts: (<b>a</b>) O1s; (<b>b</b>) V2p; (<b>c</b>) Mo3d.</p>
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<p>System diagram of a denitrification unit.</p>
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19 pages, 5651 KiB  
Article
Advanced Dentistry Biomaterials Containing Graphene Oxide
by Doina Prodan, Marioara Moldovan, Stanca Cuc, Codruţa Sarosi, Ioan Petean, Miuța Filip, Rahela Carpa, Rami Doukeh and Ioana-Codruta Mirica
Polymers 2024, 16(12), 1743; https://doi.org/10.3390/polym16121743 - 19 Jun 2024
Viewed by 607
Abstract
The aim of this study was to obtain three experimental resin-based cements containing GO and HA-Ag for posterior restorations. The samples (S0, S1, and S2) shared the same polymer matrix (BisGMA, TEGDMA) and powder mixture (bioglass (La2O3 and Sr-Zr), quartz, [...] Read more.
The aim of this study was to obtain three experimental resin-based cements containing GO and HA-Ag for posterior restorations. The samples (S0, S1, and S2) shared the same polymer matrix (BisGMA, TEGDMA) and powder mixture (bioglass (La2O3 and Sr-Zr), quartz, GO, and HA-Ag), with different percentages of graphene oxide (0%, 0.1%, 0.2% GO) and silver-doped hydroxyapatite (10%, 9.9%, 9.8% HA-Ag). The physical–chemical properties (water absorption, degree of conversion), mechanical properties (DTS, CS, FS), structural properties (SEM, AFM), and antibacterial properties (Staphylococcus aureus, Enterococcus faecalis, Streptococcus mutans, Porphyromonas gingivalis, and Escherichia coli) were investigated. The results showed that the mechanical properties, except for the diametral tensile test, increased with the rise in the %GO. After 28 days, water absorption increased with the rise in the %GO. The surface structure of the samples did not show major changes after water absorption for 28 days. The antibacterial effects varied depending on the samples and bacterial strains tested. After increasing the %GO and decreasing the %HA-Ag, we observed a more pronounced antibacterial effect. The presence of GO, even in very small percentages, improved the properties of the tested experimental cements. Full article
(This article belongs to the Special Issue Functional Graphene-Polymer Composites)
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<p>The bacterial strains studied and the samples (S0, S1, and S2) tested (Sa—<span class="html-italic">Staphylococcus aureus</span>, Ec—<span class="html-italic">Escherichia coli</span>, Ef—<span class="html-italic">Enterococcus faecalis</span>, Pg—<span class="html-italic">Porphyromonas gingivalis</span>, Sm—<span class="html-italic">Streptococcus mutans</span>).</p>
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<p>The degree of conversion of the liquid sample and of the cement samples immediately cured and 24 h after polymerization.</p>
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<p>Stress–strain curves for the mechanical tests.</p>
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<p>Water absorption of sample S0 (without GO) and samples S1 and S2 (with 0.1% and 2% GO, respectively) after 1, 2, 3, 7, 10, 14, 21, and 28 days.</p>
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<p>SEM images on the surface of samples S0 (<b>a</b>,<b>d</b>), S1 (<b>b</b>,<b>e</b>), and S2 (<b>c</b>,<b>f</b>) before the water absorption test (<b>a</b>–<b>c</b>) and after 28 days of storage in water (<b>d</b>–<b>f</b>).</p>
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<p>AFM images of the samples’ fine microstructures before liquid immersion: (<b>a</b>) S0, (<b>b</b>) S1, (<b>c</b>) S2 and after liquid immersion for 28 days: (<b>d</b>) S0, (<b>e</b>) S1, and (<b>f</b>) S2.</p>
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<p>AFM images of the sample’s nanostructure before liquid immersion: (<b>a</b>) S0, (<b>b</b>) S1, (<b>c</b>) S2 and after liquid immersion for 28 days: (<b>d</b>) S0, (<b>e</b>) S1, (<b>f</b>) S2.</p>
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<p>Surface roughness variation for the (<b>a</b>) fine microstructure and (<b>b</b>) nanostructure.</p>
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<p>Antibacterial activity of the cement samples (S0, S1, S2), after 48 h of incubation against Sa—<span class="html-italic">Staphylococcus aureus</span>, Ec—<span class="html-italic">Escherichia coli</span>, Ef—<span class="html-italic">Enterococcus faecalis</span>, Pg—<span class="html-italic">Porphyromonas gingivalis</span>, Sm—<span class="html-italic">Streptococcus mutans</span>.</p>
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