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12 pages, 3358 KiB  
Article
Water-Soluble Sacrificial Layer of Sr3Al2O6 for the Synthesis of Free-Standing Doped Ceria and Strontium Titanate
by Simone Sanna, Olga Krymskaya and Antonello Tebano
Appl. Sci. 2025, 15(4), 2192; https://doi.org/10.3390/app15042192 - 19 Feb 2025
Viewed by 364
Abstract
Epitaxial layers of water-soluble Sr3Al2O6 were fabricated as sacrificial layers on SrTiO3 (100) single-crystal substrates using the Pulsed Laser Deposition technique. This approach envisages the possibility of developing a new generation of micro-Solid Oxide Fuel Cells and [...] Read more.
Epitaxial layers of water-soluble Sr3Al2O6 were fabricated as sacrificial layers on SrTiO3 (100) single-crystal substrates using the Pulsed Laser Deposition technique. This approach envisages the possibility of developing a new generation of micro-Solid Oxide Fuel Cells and micro-Solid Oxide Electrochemical Cells for portable energy conversion and storage devices. The sacrificial layer technique offers a pathway to engineering free-standing membranes of electrolytes, cathodes, and anodes with total thicknesses on the order of a few nanometers. Furthermore, the ability to etch the SAO sacrificial layer and transfer ultra-thin oxide films from single-crystal substrates to silicon-based circuits opens possibilities for creating a novel class of mixed electronic and ionic devices with unexplored potential. In this work, we report the growth mechanism and structural characterization of the SAO sacrificial layer. Epitaxial samarium-doped ceria films, grown on SrTiO3 substrates using Sr3Al2O6 as a buffer layer, were successfully transferred onto silicon wafers. This demonstration highlights the potential of the sacrificial layer method for integrating high-quality oxide thin films into advanced device architectures, bridging the gap between oxide materials and silicon-based technologies. Full article
(This article belongs to the Special Issue Advanced Materials for Photoelectrochemical Energy Conversion)
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Figure 1

Figure 1
<p>XRD patterns in θ-2θ scan mode, respectively: (<b>a</b>) STO/SAO/STO and (<b>b</b>) STO onto PDMS.</p>
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<p>XRD patterns in θ-2θ scan mode, respectively: (<b>a</b>) GDC/SAO/STO and (<b>b</b>) GDC onto PDMS.</p>
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<p>XRD patterns in θ-2θ scan mode, respectively: (<b>a</b>) SDC/SAO/STO and (<b>b</b>) SDC onto PDMS.</p>
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<p>The Reflection High-Energy Electron Diffraction (RHEED) pattern evolution during the PLD process: STO (100) single crystal (<b>a</b>); SAO/STO (<b>b</b>); SDC/SAO/STO (<b>c</b>).</p>
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<p>FE-SEM images of SDC free-standing membrane onto PDMS at 40X (<b>a</b>) and 10 KX (<b>b</b>).</p>
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<p>Electrochemical cell fabrication procedure with sacrificial layer method.</p>
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20 pages, 11484 KiB  
Article
Tunable Filters Using Defected Ground Structures at Millimeter-Wave Frequencies
by Kaushik Annam, Birhanu Alemayehu, Eunsung Shin and Guru Subramanyam
Micromachines 2025, 16(1), 60; https://doi.org/10.3390/mi16010060 - 31 Dec 2024
Viewed by 798
Abstract
This paper explores the potential of phase change materials (PCM) for dynamically tuning the frequency response of a dumbbell u-slot defected ground structure (DGS)-based band stop filter. The DGSs are designed using co-planar waveguide (CPW) line structure on top of a barium strontium [...] Read more.
This paper explores the potential of phase change materials (PCM) for dynamically tuning the frequency response of a dumbbell u-slot defected ground structure (DGS)-based band stop filter. The DGSs are designed using co-planar waveguide (CPW) line structure on top of a barium strontium titanate (Ba0.6Sr0.4TiO3) (BST) thin film. BST film is used as the high-dielectric material for the planar DGS. Lower insertion loss of less than −2 dB below the lower cutoff frequency, and enhanced band-rejection with notch depth of −39.64 dB at 27.75 GHz is achieved by cascading two-unit cells, compared to −12.26 dB rejection with a single-unit cell using BST thin film only. Further tunability is achieved by using a germanium telluride (GeTe) PCM layer. The electrical properties of PCM can be reversibly altered by transitioning between amorphous and crystalline phases. We demonstrate that incorporating a PCM layer into a DGS device allows for significant tuning of the resonance frequency: a shift in resonance frequency from 30.75 GHz to 33 GHz with a frequency shift of 2.25 GHz is achieved, i.e., 7.32% tuning is shown with a single DGS cell. Furthermore, by cascading two DGS cells with PCM, an even wider tuning range is achievable: a shift in resonance frequency from 27 GHz to 30.25 GHz with a frequency shift of 3.25 GHz is achieved, i.e., 12.04% tuning is shown by cascading two DGS cells. The results are validated through simulations and measurements, showcasing excellent agreement. Full article
(This article belongs to the Special Issue Microwave Passive Components, 2nd Edition)
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<p>Dumbbell DGS on CPW line.</p>
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<p>U-slot DGS on CPW line.</p>
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<p>Dumbbell u-slot DGS on CPW line.</p>
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<p>Schematic representation of the fabrication process of a dumbbell u-slot DGS using CPW line configuration with BST thin film.</p>
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<p>(<b>a</b>) Simulated frequency response of dumbbell u-slot DGS. (<b>b</b>) Measured frequency response of dumbbell u-slot DGS. (<b>c</b>) Simulated vs. measured S<sub>21</sub> frequency response of dumbbell u-slot DGS.</p>
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<p>(<b>a</b>) Simulated frequency response of dumbbell u-slot DGS. (<b>b</b>) Measured frequency response of dumbbell u-slot DGS. (<b>c</b>) Simulated vs. measured S<sub>21</sub> frequency response of dumbbell u-slot DGS.</p>
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<p>Simulated vs. measured S<sub>21</sub> frequency response of dumbbell DGS.</p>
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<p>Simulated vs. measured S<sub>21</sub> frequency response of u-slot DGS.</p>
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<p>Circuit model for dumbbell u-slot DGS.</p>
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<p>Dumbbell u-slot DGS cascade.</p>
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<p>(<b>a</b>) Simulated frequency response of cascaded dumbbell u-slot DGS. (<b>b</b>) Measured frequency response of cascaded dumbbell u-slot DGS. (<b>c</b>) Simulated vs. measured S<sub>21</sub> frequency response of cascaded dumbbell u-slot DGS.</p>
Full article ">Figure 10 Cont.
<p>(<b>a</b>) Simulated frequency response of cascaded dumbbell u-slot DGS. (<b>b</b>) Measured frequency response of cascaded dumbbell u-slot DGS. (<b>c</b>) Simulated vs. measured S<sub>21</sub> frequency response of cascaded dumbbell u-slot DGS.</p>
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<p>Circuit model for cascaded dumbbell u-slot DGS.</p>
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<p>Schematic model vs. measured S<sub>21</sub> frequency response of cascade dumbbell u-slot DGS.</p>
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<p>Dumbbell u-slot DGS on CPW line with PCM.</p>
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<p>Schematic representation of the fabrication process of a dumbbell u-slot DGS using CPW line configuration with BST and GeTe thin films.</p>
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<p>Frequency response of dumbbell u-slot DGS with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured S<sub>21</sub>—amorphous state. (<b>f</b>) Simulation vs measured S<sub>21</sub>—crystalline state.</p>
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<p>Frequency response of dumbbell u-slot DGS with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured S<sub>21</sub>—amorphous state. (<b>f</b>) Simulation vs measured S<sub>21</sub>—crystalline state.</p>
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<p>Frequency response of dumbbell u-slot DGS with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured S<sub>21</sub>—amorphous state. (<b>f</b>) Simulation vs measured S<sub>21</sub>—crystalline state.</p>
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<p>Dumbbell u-slot DGS with PCM cascade.</p>
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<p>Frequency response of dumbbell u-slot DGS cascade with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured—amorphous state. (<b>f</b>) Simulation vs measured—crystalline state.</p>
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<p>Frequency response of dumbbell u-slot DGS cascade with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured—amorphous state. (<b>f</b>) Simulation vs measured—crystalline state.</p>
Full article ">Figure 17 Cont.
<p>Frequency response of dumbbell u-slot DGS cascade with PCM. (<b>a</b>) Simulation—amorphous state. (<b>b</b>) Simulation—crystalline state. (<b>c</b>) Measured—amorphous state. (<b>d</b>) Measured—crystalline state. (<b>e</b>) Simulation vs measured—amorphous state. (<b>f</b>) Simulation vs measured—crystalline state.</p>
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16 pages, 5705 KiB  
Article
Performance and Characterization of Additively Manufactured BST Varactor Enhanced by Photonic Thermal Processing
by Carlos Molina, Ugur Guneroglu, Adnan Zaman, Liguan Li and Jing Wang
Crystals 2024, 14(11), 990; https://doi.org/10.3390/cryst14110990 - 16 Nov 2024
Viewed by 948
Abstract
The demand for reconfigurable devices for emerging RF and microwave applications has been growing in recent years, with additive manufacturing and photonic thermal treatment presenting new possibilities to supplement conventional fabrication processes to meet this demand. In this paper, we present the realization [...] Read more.
The demand for reconfigurable devices for emerging RF and microwave applications has been growing in recent years, with additive manufacturing and photonic thermal treatment presenting new possibilities to supplement conventional fabrication processes to meet this demand. In this paper, we present the realization and analysis of barium–strontium–titanate-(Ba0.5Sr0.5TiO3)-based ferroelectric variable capacitors (varactors), which are additively deposited on top of conventionally fabricated interdigitated capacitors and enhanced by photonic thermal processing. The ferroelectric solution with suspended BST nanoparticles is deposited on the device using an ambient spray pyrolysis method and is sintered at low temperatures using photonic thermal processing by leveraging the high surface-to-volume ratio of the BST nanoparticles. The deposited film is qualitatively characterized using SEM imaging and XRD measurements, while the varactor devices are quantitatively characterized by using high-frequency RF measurements from 300 MHz to 10 GHz under an applied DC bias voltage ranging from 0 V to 50 V. We observe a maximum tunability of 60.6% at 1 GHz under an applied electric field of 25 kV/mm (25 V/μm). These results show promise for the implementation of photonic thermal processing and additive manufacturing as a means to integrate reconfigurable ferroelectric varactors in flexible electronics or tightly packaged on-chip applications, where a limited thermal budget hinders the conventional thermal processing. Full article
(This article belongs to the Special Issue Ceramics: Processes, Microstructures, and Properties)
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<p>(<b>a</b>) Diagram of IDC device fabricated with key dimensions labeled; (<b>b</b>) diagram depicting how BST is deposited to only cover the finger area; (<b>c</b>) microscope image of fabricated electrode layer; (<b>d</b>) SEM image of a device after BST deposition.</p>
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<p>Diagram of ambient spray pyrolysis setup.</p>
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<p>(<b>a</b>) Magnitude of the reflection coefficient (<span class="html-italic">S</span><sub>11</sub>) of the BST IDC device under a varied bias voltage (0–50 V), and (<b>b</b>) phase of the reflection coefficient of the BST IDC device under a varied bias voltage (0–50 V).</p>
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<p>(<b>a</b>) Real part of the calculated <span class="html-italic">Z</span><sub>11</sub> (impedance) for different bias conditions, (<b>b</b>) imaginary part of the calculated <span class="html-italic">Z</span><sub>11</sub> (reactance) for different bias conditions, (<b>c</b>) calculated capacitance for the IDC device under different bias conditions, and (<b>d</b>) zoomed-in region of the calculated capacitance versus the frequency below 3 GHz.</p>
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<p>(<b>a</b>) Real part of the calculated <span class="html-italic">Z</span><sub>11</sub> (impedance) for different bias conditions, (<b>b</b>) imaginary part of the calculated <span class="html-italic">Z</span><sub>11</sub> (reactance) for different bias conditions, (<b>c</b>) calculated capacitance for the IDC device under different bias conditions, and (<b>d</b>) zoomed-in region of the calculated capacitance versus the frequency below 3 GHz.</p>
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<p>(<b>a</b>) Tunability vs. frequency of a measured IDC device at various bias voltages, and (<b>b</b>) zoomed-in tunability vs. frequency for a reduced frequency range up to 3 GHz, over which the tunability exhibits quasi-constant values.</p>
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<p>(<b>a</b>) Graph of the derived dielectric constant, and (<b>b</b>) zoomed-in dielectric constant graph.</p>
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<p>Calculated <span class="html-italic">Q</span> Factor of the IDC device as a function of frequency under various bias voltages.</p>
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<p>(<b>a</b>) Calculated loss tangent vs. frequency at a varied bias voltage (0–50 V), and (<b>b</b>) zoomed-in loss tangent vs. frequency at a reduced frequency range up to 3 GHz under a varied bias voltage (0–50 V).</p>
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<p>SEM images of the BST film deposited on the IDC device at different magnifications: (<b>a</b>) 240× magnification, (<b>b</b>) 1000× magnification, (<b>c</b>) 4000× magnification, and (<b>d</b>) 8000× magnification.</p>
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<p>SEM images of the BST film deposited on the IDC device at different magnifications: (<b>a</b>) 240× magnification, (<b>b</b>) 1000× magnification, (<b>c</b>) 4000× magnification, and (<b>d</b>) 8000× magnification.</p>
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<p>(<b>a</b>) Full span two-theta XRD scan of the BST film after the photonic thermal processing (unlabeled peaks correspond to Kβ), and (<b>b</b>) a comparison of XRD responses of as-deposited and thermally processed BST films.</p>
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<p>(<b>a</b>) Full span two-theta XRD scan of the BST film after the photonic thermal processing (unlabeled peaks correspond to Kβ), and (<b>b</b>) a comparison of XRD responses of as-deposited and thermally processed BST films.</p>
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15 pages, 15469 KiB  
Article
Unveiling BaTiO3-SrTiO3 as Anodes for Highly Efficient and Stable Lithium-Ion Batteries
by Nischal Oli, Nawraj Sapkota, Brad R. Weiner, Gerardo Morell and Ram S. Katiyar
Nanomaterials 2024, 14(21), 1723; https://doi.org/10.3390/nano14211723 - 29 Oct 2024
Viewed by 1326
Abstract
Amidst the swift expansion of the electric vehicle industry, the imperative for alternative battery technologies that balance economic feasibility with sustainability has reached unprecedented importance. Herein, we utilized Perovskite-based oxide compounds barium titanate (BaTiO3) and strontium titanate (SrTiO3) nanoparticles [...] Read more.
Amidst the swift expansion of the electric vehicle industry, the imperative for alternative battery technologies that balance economic feasibility with sustainability has reached unprecedented importance. Herein, we utilized Perovskite-based oxide compounds barium titanate (BaTiO3) and strontium titanate (SrTiO3) nanoparticles as anode materials for lithium-ion batteries from straightforward and standard carbonate-based electrolyte with 10% fluoroethylene carbonate (FEC) additive [1M LiPF6 (1:1 EC: DEC) + 10% FEC]. SrTiO3 and BaTiO3 electrodes can deliver a high specific capacity of 80 mA h g−1 at a safe and low average working potential of ≈0.6 V vs. Li/Li+ with excellent high-rate performance with specific capacity of ~90 mA h g−1 at low current density of 20 mA g−1 and specific capacity of ~80 mA h g−1 for over 500 cycles at high current density of 100 mA g−1. Our findings pave the way for the direct utilization of perovskite-type materials as anode materials in Li-ion batteries due to their promising potential for Li+ ion storage. This investigation addresses the escalating market demands in a sustainable manner and opens avenues for the investigation of diverse perovskite oxides as advanced anodes for next-generation metal-ion batteries. Full article
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Graphical abstract

Graphical abstract
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<p>(<b>a</b>) XRD pattern SrTiO<sub>3</sub> (STO). (<b>b</b>) Crystal structure of STO. (<b>c</b>) Raman shifts of STO. (<b>d</b>) XRD pattern of BaTiO<sub>3</sub> (BTO). (<b>e</b>) Crystal structure of BTO. (<b>f</b>) Raman shifts of BTO.</p>
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<p>SEM images of BTO and STO. (<b>a</b>) BTO at 200 nm. (<b>b</b>) BTO at 500 nm. (<b>c</b>) STO at 200 nm. (<b>d</b>) STO at 500 nm.</p>
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<p>SEM mapping images of BTO and STO at 2 µm. (<b>a</b>–<b>d</b>) Ba, Ti, O, and BaTiO<sub>3</sub>, respectively. (<b>e</b>–<b>h</b>) Sr, Ti, O, and SrTiO<sub>3</sub>, respectively.</p>
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<p>Electrochemical performance of BTO at different voltage ranges in LIBs. (<b>a</b>) Galvanostatic charge–discharge (GCD) at 0.001–1.5 V. (<b>b</b>) Cyclic performance at 0.001–1.5 V. (<b>c</b>) Galvanostatic charge–discharge (GCD) at 0.001–2.0 V. (<b>d</b>) Cyclic performance at 0.001–2.0 V.</p>
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<p>Electrochemical performance of STO at different voltage ranges in LIBs. (<b>a</b>) Galvanostatic charge–discharge (GCD) at 0.001–1.5 V. (<b>b</b>) Cyclic performance at 0.001–1.5 V. (<b>c</b>) Galvanostatic charge–discharge (GCD) at 0.001–2.0 V. (<b>d</b>) Cyclic performance at 0.001–2.0 V.</p>
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<p>Rate performance of STO and BTO in 0.001–1.5 V. (<b>a</b>) STO rate performance in the range of 20 to 150 mA g<sup>−1</sup>. (<b>b</b>) STO rate curve profile at different current densities in the range of 20 to 150 mA g<sup>−1</sup>. (<b>c</b>) BTO rate performance in the range of 20 to 150 mA g<sup>−1</sup>. (<b>d</b>) BTO discharge/charge voltage profile at different current densities in the range of 20 to 150 mA g<sup>−1</sup>.</p>
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<p>Cyclic voltammetry (CV) curves of the BTO and STO at room temperature. (<b>a</b>) CV of BTO in the first 3 cycles at a scan rate of 0.1 mV s<sup>−1</sup>. (<b>b</b>) CV of BTO in the different scan rates of 0.1–1.2 mV s<sup>−1</sup>. (<b>c</b>) CV of STO in the first 3 cycles at a scan rate of 0.1 mV s<sup>−1</sup>. (<b>d</b>) CV of STO in the different scan rates of 0.1–1.2 mV s<sup>−1</sup>.</p>
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<p>(<b>a</b>) Peak current (i) vs. v<sup>1/2</sup> (square root of scan rate (v)) of BTO. (<b>b</b>) Log (i) (peak current (i)) vs. log (v) (scan rate (v)) of STO. (<b>c</b>) Log (i) vs. log (v) of BTO and STO.</p>
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<p>X-ray photoelectron spectroscopy (XPS) measurement. (<b>a</b>) Pristine STO, lithiation (discharge), lithiation–delithiation (discharge–charge), after 3 cycles. (<b>b</b>) O1s. (<b>c</b>) STO survey different conditions. (<b>d</b>) Pristine BTO, lithiation (discharge), lithiation–delithiation (discharge–charge), after 3 cycles. (<b>e</b>) O1s. (<b>f</b>) BTO survey different conditions.</p>
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<p>Electrochemical impedance spectroscopy (EIS) STO- and BTO-based electrodes. (<b>a</b>) STO before charging. (<b>b</b>) STO after 40 charge–discharge. (<b>c</b>) BTO before charging. (<b>d</b>) BTO after 40 cycles.</p>
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14 pages, 2483 KiB  
Article
Enhanced Crystallinity of SrTiO3 Films on a Silicon Carbide Substrate: Structural and Microwave Characterization
by Andrei Tumarkin, Eugene Sapego, Alexey Bogdan, Artem Karamov, Igor Serenkov and Vladimir Sakharov
Appl. Sci. 2024, 14(21), 9672; https://doi.org/10.3390/app14219672 - 23 Oct 2024
Viewed by 2893
Abstract
Thin films of strontium titanate, which reveal high structure quality and tunable properties prospective for microwave applications at room temperature, were grown on a semi-insulating silicon carbide substrate using magnetron sputtering for the first time. The films’ growth mechanisms were studied using medium-energy [...] Read more.
Thin films of strontium titanate, which reveal high structure quality and tunable properties prospective for microwave applications at room temperature, were grown on a semi-insulating silicon carbide substrate using magnetron sputtering for the first time. The films’ growth mechanisms were studied using medium-energy ion scattering, and the films’ structures were investigated using X-ray diffraction. The electrical characteristics of planar capacitors based on strontium titanate films were measured at a frequency of 2 GHz using a high-precision resonance technique. It is shown that the tendency to improve the crystalline structure of strontium titanate film with an increase in the substrate temperature is most pronounced for films deposited at elevated working gas pressure under low supersaturation conditions. Planar capacitors formed on the basis of oriented SrTiO3 films on silicon carbide showed tunability n = 36%, with a loss tangent of 0.008–0.009 at a level of slow relaxation of capacitance, which is significantly lower than the data published currently regarding planar tunable ferroelectric elements. This is the first successful attempt to realize a planar SrTiO3 capacitor on a silicon carbide substrate, which exhibits a commutation quality factor more than 2500 at microwaves. Full article
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Figure 1
<p>MEIS spectra of STO films obtained at pressures of 6 and 10 Pa and at substrate temperatures of 800–900 °C.</p>
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<p>The height of the islands and the degree of coating of the substrate with islands for STO films grown at T<sub>s</sub> = 800 °C.</p>
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<p>Diffractograms of films obtained at different substrate temperatures and different working gas pressures.</p>
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<p>Diffractograms of films of different thicknesses obtained at a pressure of 10 Pa and a substrate temperature of 900 °C.</p>
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<p>AFM image of a STO film surface on a SiC substrate.</p>
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<p>Normalized capacitance and response time parameters of capacitors obtained at different working gas pressures.</p>
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<p>Quality factor of capacitors obtained at different working gas pressures.</p>
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18 pages, 7530 KiB  
Article
Investigating the Synergistic Effect of Decoration and Doping in Silver/Strontium Titanate for Air Remediation
by Marcela Frías Ordóñez, Elisabetta Sacco, Marco Scavini, Giuseppina Cerrato, Alessia Giordana, Ermelinda Falletta and Claudia Letizia Bianchi
Nanomaterials 2024, 14(20), 1663; https://doi.org/10.3390/nano14201663 - 16 Oct 2024
Cited by 1 | Viewed by 1018
Abstract
Strontium titanate (STO) and its variants have emerged as leading materials in photocatalysis, particularly for degrading nitrogen oxides (NOx), due to their non-toxic nature, structural adaptability, and exceptional thermal stability. Although the one-pot sol-gel method leads to high-quality photocatalysts, areas remain for improvement. [...] Read more.
Strontium titanate (STO) and its variants have emerged as leading materials in photocatalysis, particularly for degrading nitrogen oxides (NOx), due to their non-toxic nature, structural adaptability, and exceptional thermal stability. Although the one-pot sol-gel method leads to high-quality photocatalysts, areas remain for improvement. This study examines the impact of ethanol as a cosolvent in STO synthesis, focusing on optimizing the water-to-ethanol volume ratio. The findings reveal that a 1:3 ratio significantly enhances macropore formation and photocatalytic efficiency, achieving 42% NOx degradation under LED within three hours. Furthermore, incorporating 8.0 wt.% Ag into STO substantially improves visible light absorption and enables complete NOx elimination, thanks to enhanced charge separation and localized surface plasmon resonance. Even at high temperatures (1100 °C), the Ag-STO photocatalyst maintains partial activity, despite exceeding silver’s melting point. These results highlight the potential of STO-based materials for industrial applications, positioning them as a promising solution for effective NOx mitigation. Full article
(This article belongs to the Special Issue Advanced Nanomaterials for Photocatalysis)
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Graphical abstract

Graphical abstract
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<p>Schematic representation of the experimental set-up employed for the NOx photodegradation.</p>
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<p>Experimental patterns of STO (black curve), 2.5% Ag-STO (red curve), 5.8% Ag-STO (blue curve), and 8.0% Ag-STO (pink curve).</p>
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<p>Panel (<b>A</b>): Complete experimental XRD pattern of 8.0 wt.% Ag-STO sample (black symbol) together with its Rietveld refinement (red curve) and the difference curve (blue curve). The inset highlights the high-angle data and refined curve. Panel (<b>B</b>): Details of the same pattern corresponding to the (111) reflection of Ag phase(s). Black symbols are the experimental data; blue and green curves show the contribution of “Ag-broad” and “Ag-sharp” phases to the peak while the red curve is their sum. See the main text for details. Panel (<b>C</b>): Williamson–Hall plot for the Ag-broad phase.</p>
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<p>FE-SEM images of 8 wt.% Ag-STO_1100C with (<b>a</b>) 2 h, (<b>b</b>) 10 h, and (<b>c</b>) 15 h of heat treatment.</p>
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<p>FE-SEM images of (<b>a</b>) STO (1:3), (<b>b</b>) STO (1:5), and (<b>c</b>) 8 wt.% Ag-STO.</p>
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<p>SEM image (<b>a</b>), elemental mapping of strontium (<b>b</b>), titanium (<b>c</b>), oxygen (<b>d</b>), carbon (<b>e</b>), and EDX spectrum (<b>f</b>) of STO (1:3) photocatalyst.</p>
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<p>SEM image (<b>a</b>), elemental mapping of strontium (<b>b</b>), titanium (<b>c</b>), oxygen (<b>d</b>), silver (<b>e</b>), carbon (<b>f</b>), and EDX spectrum (<b>g</b>) of 8 wt.% Ag-STO photocatalyst.</p>
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<p>HR-TEM images of 8 wt.% Ag-STO calcined at increasing temperatures and for different times. Section (<b>a</b>): sample calcined at 900 °C; Section (<b>b</b>): sample calcined at 1100 °C for 2 h; Section (<b>c</b>): sample calcined at 1100 °C for 15 h.</p>
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<p>N<sub>2</sub> adsorption/desorption isotherms at −196 °C.</p>
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<p>UV-DRS spectra of (<b>a</b>) Ag-STO photocatalysts at 900 °C and (<b>b</b>) 8 wt.% Ag-STO_1100C treated at different time conditions (2, 10, 15 h).</p>
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<p>(<b>a</b>) NOx photocatalytic removal efficiency reported as C/Co as a function of time, (<b>b</b>) photocatalytic kinetic studies of the synthesized STO and Ag-STO photocatalysts, (<b>c</b>) reusability of 8.0 wt.% Ag-STO photocatalyst for NOx degradation under LED irradiation.</p>
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10 pages, 6089 KiB  
Article
Reset-Voltage Controlled Resistance-State and Applications of Forming-Free Fe-Doped SrTiO3 Thin-Film Memristor
by Ke-Jing Lee, Cheng-Hua Wu, Cheng-Jung Lee, Dei-Wei Chou, Na-Fu Wang and Yeong-Her Wang
Materials 2024, 17(20), 5021; https://doi.org/10.3390/ma17205021 - 14 Oct 2024
Viewed by 1049
Abstract
In this study, we prepared a strontium ferrite titanate (STF) thin film using a sol–gel process to insulate resistive random-access memory (RRAM) applications. Compared to the typical strontium titanate (STO) RRAM, the improvement in the resistive switching characteristics in STF RRAM is obvious. [...] Read more.
In this study, we prepared a strontium ferrite titanate (STF) thin film using a sol–gel process to insulate resistive random-access memory (RRAM) applications. Compared to the typical strontium titanate (STO) RRAM, the improvement in the resistive switching characteristics in STF RRAM is obvious. The Al/STO/ITO/Glass RRAM set/reset voltages of −1.4 V/+3.3 V and the Al/STF/ITO/Glass RRAM set/reset voltages of −0.45 V/+1.55 V presented a memory window larger than 103, a low operating voltage and device stability of more than 104 s. In this study, the influence of Fe on the conducting paths and the bipolar resistive switching properties of Al/STF/ITO/Glass RRAM devices is investigated. Full article
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<p>The surface morphologies of (<b>a</b>) STO, and (<b>b</b>) STF thin films inspected by AFM. (<b>c</b>) XRD pattern of STO and STF thin film. (<b>d</b>) XPS full spectra analysis of the STO, and STF thin films.</p>
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<p>I-V characteristics of Al/STO/ITO and Al/STF/ITO RRAM device.</p>
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<p>C-AFM (5 × 5 μm<sup>2</sup> area) measurement of (<b>a</b>) STO and (<b>b</b>) STF structure.</p>
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<p>LogI–logV plots of (<b>a</b>) STO device and (<b>b</b>) STF device at LRS and HRS.</p>
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<p>XPS narrow-scan spectra for all compositions in the surface of SFT thin film of (<b>a</b>) Sr 3d (<b>b</b>) Ti 2p (<b>c</b>) O 1s and (<b>d</b>) Fe 2p.</p>
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<p>(<b>a</b>) Temperature-dependent resistance of STO and STF RRAM device measured between 300 K and 400 K. (<b>b</b>) LRS current versus cell area of STO and STF memory devices.</p>
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<p>Statistical distributions of (<b>a</b>) current values and (<b>b</b>) voltage values of Al/STO/ITO and Al/STF/ITO structure.</p>
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<p>(<b>a</b>) DC cycle endurance and (<b>b</b>) retention characteristics of STO and STF RRAM device at 0.1 V under room temperature.</p>
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<p>Resistive switching mechanism model of the STF-based RRAM.</p>
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<p>(<b>a</b>) Schematic of the Al/STF/ITO device, (<b>b</b>) FIB cross-section image of the fabricated device.</p>
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14 pages, 5056 KiB  
Article
Fractal Analysis of Doped Strontium Titanate Photocatalyst
by Ivana Stajcic, Cristina Serpa, Bojana Simovic, Ivona Jankovic Castvan, Vladimir Dodevski, Vesna Radojevic and Aleksandar Stajcic
Fractal Fract. 2024, 8(10), 560; https://doi.org/10.3390/fractalfract8100560 - 27 Sep 2024
Viewed by 899
Abstract
In this research, the doping of SrTiO3 with Mn4+ was performed in order to evaluate the potential application as a photocatalyst for the degradation of organic dye pollutants. Since photocatalytic activity depends on grain microstructure, fractal analysis was used to estimate [...] Read more.
In this research, the doping of SrTiO3 with Mn4+ was performed in order to evaluate the potential application as a photocatalyst for the degradation of organic dye pollutants. Since photocatalytic activity depends on grain microstructure, fractal analysis was used to estimate the Hausdorff dimension to provide a more thorough investigation of Mn@SrTiO3 morphology. Structural analysis by infrared spectroscopy indicated the incorporation of Mn4+ into the SrTiO3 lattice, while by using x-ray diffraction, the crystallite size of 44 nm was determined. The photocatalytic activity test performed on complex ethyl violet organic dye revealed potential for Mn@SrTiO3 application in water treatment. Based on fractal regression analysis, a good estimate was obtained for the reconstruction of grain shape, with a Hasudorff dimension of 1.13679, which was used to find the best kinetics model for the photodegradation reaction. The experimental data showed a nearly linear fit with fractal-like pseudo-zero order. These findings and applications of fractal dimensions could contribute to future characterizations of photocatalysts, providing a deeper understanding of surface properties and their influence on photocatalytic activity. Full article
(This article belongs to the Section Mathematical Physics)
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<p>FTIR spectra of hybrid SrTiO<sub>3</sub>/MnO<sub>2</sub> and Mn@SrTiO<sub>3</sub>.</p>
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<p>XRD pattern of the modified SrTiO<sub>3</sub>.</p>
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<p>Williamson–Hall plot of <span class="html-italic">β</span>cos<span class="html-italic">ϴ</span> vs. sin<span class="html-italic">ϴ</span> of modified SrTiO<sub>3</sub>.</p>
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<p>FESEM images of sintered Mn@SrTiO<sub>3</sub>.</p>
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<p>Adsorption and photodegradation of EV dye in the presence of modified SrTiO<sub>3</sub> nanopowder.</p>
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<p>The structural formula of cationic EV dye used in photocatalytic experiment shown by the MolView 3D v2.4. modeling software (C—grey; N—blue; H—white spheres).</p>
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<p>(<b>a</b>) Plots of <span class="html-italic">c</span><sub>0</sub><span class="html-italic">−c</span>, (<b>b</b>) plots of ln(<span class="html-italic">c</span><sub>0</sub>/<span class="html-italic">c</span>), and (<b>c</b>) plots of 1/<span class="html-italic">c</span>−1/<span class="html-italic">c</span><sub>0</sub> versus time for the photodegradation of cationic EV dye in the presence of modified SrTiO<sub>3</sub> under simulated solar light for 180 min.</p>
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<p>Enlarged Mn@SrTiO<sub>3</sub> grain (<b>left</b>) and estimated fractal curve of grain (<b>right</b>).</p>
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<p>Original and estimated plot in Cartesian coordinate system.</p>
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<p>Fractal-like kinetics fit for photodegradation of EV.</p>
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10 pages, 2891 KiB  
Article
Forming Ni-Fe and Co-Fe Bimetallic Structures on SrTiO3-Based SOFC Anode Candidates
by Kinga Kujawska, Wojciech Koliński and Beata Bochentyn
Fuels 2024, 5(3), 564-573; https://doi.org/10.3390/fuels5030031 - 20 Sep 2024
Viewed by 962
Abstract
The aim of this work was to verify the possibility of forming Ni-Fe and Co-Fe alloys via topotactic ion exchange exsolution in Fe-infiltrated (La,Sr,Ce)0.9(Ni,Ti)O3-δ or (La,Sr,Ce)0.9(Co,Ti)O3-δ ceramics. For this purpose, samples were synthesized using the Pechini method [...] Read more.
The aim of this work was to verify the possibility of forming Ni-Fe and Co-Fe alloys via topotactic ion exchange exsolution in Fe-infiltrated (La,Sr,Ce)0.9(Ni,Ti)O3-δ or (La,Sr,Ce)0.9(Co,Ti)O3-δ ceramics. For this purpose, samples were synthesized using the Pechini method and then infiltrated with an iron nitrate solution. The reduction process in dry H2 forced the topotactic ion exchange exsolution, leading to the formation of additional round-shape structures on the surfaces of grains. EDS scans and XRD analysis confirmed the formation of bimetallic alloys, which suggests that these materials have great potential for further use as anode materials for Solid Oxide Fuel Cells (SOFCs). Full article
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<p>XRD patterns of as-prepared LSCNiT and LSCCoT powders. The inset shows a magnification of the main peaks compared for both LSCNiT and LSCCoT and a reference SrTiO<sub>3</sub> pattern.</p>
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<p>Cross-sectional SEM images of fracture surfaces of the as-prepared pellets of (<b>a</b>) LSCCoT and (<b>b</b>) LSCNiT before infiltration and reduction.</p>
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<p>Cross-sectional SEM images of fracture structures of infiltrated (<b>a</b>) LSCCoT + 15% and (<b>b</b>) LSCNiT + 15%.</p>
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<p>Cross-sectional SEM images of fracture structures of infiltrated compounds: (<b>a</b>) LSCCoT + 5%, (<b>b</b>) LSCNiT + 5%, (<b>c</b>) LSCCoT + 10%, (<b>d</b>) LSCNiT + 10%, (<b>e</b>) LSCCoT + 15%, (<b>f</b>) LSCNiT + 15%.</p>
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<p>SEM images of inspected area of (<b>a</b>) LSCCoT with 15% gain in mass weight and (<b>b</b>) LSCNiT with 15% in mass increase after infiltration with iron precursor and reduction at 1200 °C in H<sub>2</sub>. The blue arrows indicate location and direction of linear EDS scans, and scan results are shown in (<b>c</b>) LSCCoT and (<b>d</b>) LSCNiT, respectively.</p>
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<p>XRD patterns of LSCNiT + 15% and LSCCoT + 15% after infiltration with iron precursor and reduction at 1200 °C in dry H<sub>2</sub>.</p>
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17 pages, 5617 KiB  
Article
Impact of Thermochemical Treatments on Electrical Conductivity of Donor-Doped Strontium Titanate Sr(Ln)TiO3 Ceramics
by Aleksandr Bamburov, Ekaterina Kravchenko and Aleksey A. Yaremchenko
Materials 2024, 17(15), 3876; https://doi.org/10.3390/ma17153876 - 5 Aug 2024
Viewed by 1121
Abstract
The remarkable stability, suitable thermomechanical characteristics, and acceptable electrical properties of donor-doped strontium titanates make them attractive materials for fuel electrodes, interconnects, and supports of solid oxide fuel and electrolysis cells (SOFC/SOEC). The present study addresses the impact of processing and thermochemical treatment [...] Read more.
The remarkable stability, suitable thermomechanical characteristics, and acceptable electrical properties of donor-doped strontium titanates make them attractive materials for fuel electrodes, interconnects, and supports of solid oxide fuel and electrolysis cells (SOFC/SOEC). The present study addresses the impact of processing and thermochemical treatment conditions on the electrical conductivity of SrTiO3-derived ceramics with moderate acceptor-type substitution in a strontium sublattice. A-site-deficient Sr0.85La0.10TiO3−δ and cation-stoichiometric Sr0.85Pr0.15TiO3+δ ceramics with varying microstructures and levels of reduction have been prepared and characterized by XRD, SEM, TGA, and electrical conductivity measurements under reducing conditions. The analysis of the collected data suggested that the reduction process of dense donor-doped SrTiO3 ceramics is limited by sluggish oxygen diffusion in the crystal lattice even at temperatures as high as 1300 °C. A higher degree of reduction and higher electrical conductivity can be obtained for porous structures under similar thermochemical treatment conditions. Metallic-like conductivity in dense reduced Sr0.85La0.10TiO3−δ corresponds to the state quenched from the processing temperature and is proportional to the concentration of Ti3+ in the lattice. Due to poor oxygen diffusivity in the bulk, dense Sr0.85La0.10TiO3−δ ceramics remain redox inactive and maintain a high level of conductivity under reducing conditions at temperatures below 1000 °C. While the behavior and properties of dense reduced Sr0.85Pr0.15TiO3+δ ceramics with a large grain size (10–40 µm) were found to be similar, decreasing grain size down to 1–3 µm results in an increasing role of resistive grain boundaries which, regardless of the degree of reduction, determine the semiconducting behavior and lower total electrical conductivity of fine-grained Sr0.85Pr0.15TiO3+δ ceramics. Oxidized porous Sr0.85Pr0.15TiO3+δ ceramics exhibit faster kinetics of reduction compared to the Sr0.85La0.10TiO3−δ counterpart at temperatures below 1000 °C, whereas equilibration kinetics of porous Sr0.85La0.10TiO3−δ structures can be facilitated by reductive pre-treatments at elevated temperatures. Full article
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<p>Comparison of literature data on the electrical conductivity of Sr<sub>0.90</sub>La<sub>0.10</sub>TiO<sub>3±δ</sub> ceramics in reducing H<sub>2</sub>-based atmospheres. Sources: Moos [<a href="#B37-materials-17-03876" class="html-bibr">37</a>], Marina [<a href="#B36-materials-17-03876" class="html-bibr">36</a>], Yaremchenko [<a href="#B35-materials-17-03876" class="html-bibr">35</a>], Li [<a href="#B38-materials-17-03876" class="html-bibr">38</a>], Lv [<a href="#B39-materials-17-03876" class="html-bibr">39</a>], Wang [<a href="#B40-materials-17-03876" class="html-bibr">40</a>], Niwa [<a href="#B41-materials-17-03876" class="html-bibr">41</a>], Park [<a href="#B42-materials-17-03876" class="html-bibr">42</a>], and Hashimoto [<a href="#B43-materials-17-03876" class="html-bibr">43</a>]. See <a href="#materials-17-03876-t001" class="html-table">Table 1</a> for the experimental details.</p>
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<p>Examples of XRD patterns of S85L10 and S85P15 samples. Note that S85L10-1300 indicates the powder as synthesized in air at 1300 °C, and S85P15-1350 corresponds to the ceramic sample sintered in air at 1350 °C. The notations of other samples are listed in <a href="#materials-17-03876-t002" class="html-table">Table 2</a>.</p>
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<p>SEM images of fractured cross-sections of S85L10 ceramics prepared under different conditions.</p>
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<p>SEM images of fractured cross-sections of S85P15 ceramics prepared under different conditions.</p>
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<p>Electrical conductivity of S85L10 ceramics as a function of (<b>A</b>) temperature in 10%H<sub>2</sub>-N<sub>2</sub> atmosphere and (<b>B</b>) oxygen partial pressure under reducing conditions at 900 °C.</p>
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<p>(<b>A</b>) Example of thermogravimetric data recorded for powdered S85L10 (Sr<sub>0.85</sub>La<sub>0.10</sub>TiO<sub>3−δ</sub>) ceramics on cooling in 10%H<sub>2</sub>-N<sub>2</sub> atmosphere and subsequent heating/cooling cycle in air. (<b>B</b>) Electrical conductivity of dense S85L10 ceramics vs. fraction of Ti<sup>3+</sup> cations in the titanium sublattice.</p>
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<p>Relaxation of electrical conductivity of (<b>A</b>) oxidized S85L10-1320 ceramics on reduction and (<b>B</b>) reduced S85L10-1320-R-1300 ceramics on redox cycling at 900 °C.</p>
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<p>Electrical conductivity of S85P15 ceramics as a function of (<b>A</b>) temperature in 10%H<sub>2</sub>-N<sub>2</sub> atmosphere and (<b>B</b>) oxygen partial pressure under reducing conditions at 900 °C.</p>
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<p>Changes in oxygen nonstoichiometry of S85P15 (Sr<sub>0.85</sub>Pr<sub>0.15</sub>TiO<sub>3+δ</sub>) ceramics on oxidation in air estimated from the thermogravimetric data.</p>
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<p>Relaxation of electrical conductivity of porous (<b>A</b>) S85P15-1350 and (<b>B</b>) S85P15-H-1350 samples on redox cycling at 850 °C. S85P15-1350 denotes the sample sintered in air at 1350 °C for 10 h.</p>
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12 pages, 4701 KiB  
Article
Response Properties of Electrorheological Composite Hydrophilic Elastomers Based on Different Morphologies of Magnesium-Doped Strontium Titanate
by Shu-Juan Gao, Lin-Zhi Li, Peng-Fei Han, Ling Wang, Feng Li, Tan-Lai Yu and Yan-Fang Li
Molecules 2024, 29(15), 3462; https://doi.org/10.3390/molecules29153462 - 24 Jul 2024
Viewed by 1180
Abstract
As smart materials, electrorheological elastomers (EREs) formed by pre-treating active electrorheological particles are attracting more and more attention. In this work, four Mg-doped strontium titanate (Mg-STO) particles with spherical, dendritic, flake-like, and pinecone-like morphologies were obtained via hydrothermal and low-temperature co-precipitation. XRD, SEM, [...] Read more.
As smart materials, electrorheological elastomers (EREs) formed by pre-treating active electrorheological particles are attracting more and more attention. In this work, four Mg-doped strontium titanate (Mg-STO) particles with spherical, dendritic, flake-like, and pinecone-like morphologies were obtained via hydrothermal and low-temperature co-precipitation. XRD, SEM, Raman, and FT-IR were used to characterize these products. The results showed that Mg-STOs are about 1.5–2.0 μm in size, and their phase structures are dominated by cubic crystals. These Mg-STOs were dispersed in a hydrogel composite elastic medium. Then, Mg-STO/glycerol/gelatin electrorheological composite hydrophilic elastomers were obtained with or without an electric field. The electric field response properties of Mg-doped strontium titanate composite elastomers were investigated. We concluded that dendritic Mg-STO composite elastomers are high-performance EREs, and the maximum value of their energy storage was 8.70 MPa. The significant electrorheological performance of these products is helpful for their applications in vibration control, force transducers, smart structures, dampers, and other fields. Full article
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<p>SEM patterns of Mg-STO: (<b>a</b>,<b>b</b>) spherical, (<b>c</b>,<b>d</b>) dendritic, (<b>e</b>,<b>f</b>) flake-like, and (<b>g</b>,<b>h</b>) pinecone-like.</p>
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<p>XRD patterns of different Mg-STO morphologies: (a) spherical, (b) dendritic, (c) flake-like, and (d) pinecone-like.</p>
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<p>Raman patterns of different Mg-STO morphologies: (a) spherical, (b) dendritic, (c) flake-like, and (d) pinecone-like.</p>
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<p>FT-IR diagrams of four kinds of Mg-STO morphologies: (a) spherical, (b) dendritic, (c) flake-like, and (d) pinecone-like.</p>
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<p>Contact angles of water drops (3 μL) on Mg-STOs with different shapes: (<b>a</b>) spherical, (<b>b</b>) dendritic, (<b>c</b>) flake-like, and (<b>d</b>) pinecone-like.</p>
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<p>Dielectric spectra of the as-made samples: (a) spherical, (b) dendritic, (c) flake-like, and (d) pinecone-like.</p>
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<p>The energy storage modulus/frequency graphs of composite elastomers with different Mg-STOs under an electric field: (a~e) 0.0 kV/mm and (a’~e’) 1.2 kV/mm. a and a’: without Mg-STO; b and b’: with spherical Mg-STO; c and c’: with dendritic Mg-STO; d and d’: with flake-like Mg-STO; e and e’: with pinecone-like Mg-STO. The gap between curves a and a’ is labeled <span class="html-italic">d<sub>aa’</sub></span>, and others are similar.</p>
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26 pages, 7811 KiB  
Article
Enhanced Spectroscopic Insight into Acceptor-Modified Barium Strontium Titanate Thin Films Deposited via the Sol–Gel Method
by Dionizy Czekaj and Agata Lisińska-Czekaj
Materials 2024, 17(11), 2491; https://doi.org/10.3390/ma17112491 - 22 May 2024
Viewed by 1012
Abstract
In the present paper, composite thin films of barium strontium titanate (BaxSr1−xTiO3) with an acceptor modifier (magnesium oxide—MgO) were deposited on metal substrates (stainless steel type) using the sol–gel method. The composite thin films feature Bax [...] Read more.
In the present paper, composite thin films of barium strontium titanate (BaxSr1−xTiO3) with an acceptor modifier (magnesium oxide—MgO) were deposited on metal substrates (stainless steel type) using the sol–gel method. The composite thin films feature BaxSr1−xTiO3 ferroelectric solid solution as the matrix and MgO linear dielectric as the reinforcement, with MgO concentrations ranging from 1 to 5 mol%. Following thermal treatment at 650 °C, the films were analyzed for their impedance response. Experimental impedance spectra were modeled using the Kohlrausch–Williams–Watts function, revealing stretching parameters (β) in the range of approximately 0.78 to 0.89 and 0.56 to 0.90 for impedance and electric modulus formalisms, respectively. Notably, films modified with 3 mol% MgO exhibited the least stretched relaxation function. Employing the electric equivalent circuit method for data analysis, the “circle fit” analysis demonstrated an increase in capacitance from 2.97 × 10−12 F to 5.78 × 10−10 F with the incorporation of 3 mol% MgO into BST-based thin films. Further analysis based on Voigt, Maxwell, and ladder circuits revealed trends in resistance and capacitance components with varying MgO contents, suggesting non-Debye-type relaxation phenomena across all tested samples. Full article
(This article belongs to the Section Thin Films and Interfaces)
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<p>(<b>a</b>) Bode format plot of a modulus of complex impedance (|<span class="html-italic">Z</span>|) and (<b>b</b>) phase angle (<span class="html-italic">Θ</span>) vs. frequency for MgO-modified BST thin films at <span class="html-italic">T</span> = RT.</p>
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<p>Variation of the normalized (to a peak) imaginary part of impedance (<span class="html-italic">Z</span>″/<span class="html-italic">Z</span>″<sub>max</sub>) with angular frequency (<span class="html-italic">ω</span>) for different MgO contents (semi log scale).</p>
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<p>Dependence of the real part of the modulus (<span class="html-italic">M</span>′) on angular frequency at room temperature for the BST-based thin films with different amounts of MgO additive.</p>
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<p>Variations of the normalized (to a peak) imaginary part of the modulus (<span class="html-italic">M</span>″/<span class="html-italic">M</span>″<sub>max</sub>) with angular frequency (<span class="html-italic">ω</span>) for different MgO contents (semi log scale).</p>
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<p>(<b>a</b>) An example of a simulated impedance plane plot for a depressed circular arc; <span class="html-italic">β</span>-depression angle; simulation parameters: <span class="html-italic">R</span><sub>B</sub> = 0.2 MΩ; <span class="html-italic">R</span><sub>GB</sub> = 5 MΩ; <span class="html-italic">C</span> = 200 pF; and <span class="html-italic">β</span> = 0°, 18°, and 36°. (<b>b</b>) Impedance plane plot for BST-based composite thin films modified with MgO additive and measured at <span class="html-italic">T</span> = RT. Symbols—denote measured impedance data points; solid lines—results of “circle fit” of the experimental data.</p>
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<p>Circle fit parameters of the impedance data for BST thin films modified with a MgO additive, annealed at <span class="html-italic">T</span> = 650 °C: (<b>a</b>) estimated capacitance (<span class="html-italic">C</span>) and estimated resistance (<span class="html-italic">R</span>) of the grain boundary region; (<b>b</b>) estimated relaxation frequency.</p>
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<p>(<b>a</b>) Normalized imaginary part of impedance (<span class="html-italic">Z</span>″/<span class="html-italic">Z</span>″<sub>max</sub>) vs. normalized frequency (<span class="html-italic">ν/ν</span><sub>max</sub>) for different MgO contents (symbols). (<b>b</b>) A theoretical fit of <span class="html-italic">Z</span>″/<span class="html-italic">Z</span>″<sub>max</sub> vs. <span class="html-italic">ν</span>/<span class="html-italic">ν</span><sub>max</sub> performed according to the modified KWW function given by Equation (3) (semi log scale). (<b>c</b>) Histogram of the stretching parameters <span class="html-italic">β</span>. (<b>d</b>) Histogram of the relaxation times <span class="html-italic">τ</span> calculated at the base of the modified KWW function for MgO-modified BST thin films at <span class="html-italic">T</span> = RT.</p>
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<p>(<b>a</b>) Normalized imaginary part of the modulus (M″/M″<sub>max</sub>) vs. normalized frequency (<span class="html-italic">ν</span>/<span class="html-italic">ν</span><sub>max</sub>) for different MgO content (symbols). (<b>b</b>) A theoretical fit according to the modified KWW function (semi log scale). (<b>c</b>) Histogram of the stretching parameters <span class="html-italic">β</span>. (<b>d</b>) Histogram of the relaxation times <span class="html-italic">τ</span> calculated at the base of the modified KWW function for MgO-modified BST thin films at <span class="html-italic">T</span> = RT.</p>
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<p>Typical circuits used in AC modeling; they are experimentally indistinguishable: (<b>a</b>) Voigt, (<b>b</b>) Maxwell and (<b>c</b>) ladder.</p>
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<p>(<b>a</b>) Bode format plot of the modulus of complex impedance (|<span class="html-italic">Z</span>|) (log–log scale) and (<b>b</b>) phase angle (<span class="html-italic">Θ</span>) vs. frequency (semi-log scale) for the BST-based thin film modified with 3 mol% of MgO. (<b>c</b>) The impedance response of electrical equivalent circuits, namely Voigt, Maxwell and ladder, are shown in the figures (red solid line, blue dashed line and green dotted line, respectively). (<b>d</b>) Fit-quality plot for Maxwell electric equivalent circuit. For the graphs inserted in the main graph, a linear scale was used to visualize the differences in the curves.</p>
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12 pages, 4980 KiB  
Article
Indium-Doped SnO2 Based Surface Acoustic Wave Gas Sensor with Ba0.6Sr0.4TiO3 Film
by Birhanu Alemayehu, Kaushik Annam, Eunsung Shin and Guru Subramanyam
Crystals 2024, 14(4), 366; https://doi.org/10.3390/cryst14040366 - 12 Apr 2024
Cited by 3 | Viewed by 1680
Abstract
SnO2-based gas sensors have been widely synthesized and used for the detection of various hazardous gases. However, the use of doped SnO2 in sensing applications has recently attracted increased interest due to the formation of a synergistic effect between the [...] Read more.
SnO2-based gas sensors have been widely synthesized and used for the detection of various hazardous gases. However, the use of doped SnO2 in sensing applications has recently attracted increased interest due to the formation of a synergistic effect between the dopant and the host. Moreover, in the case of a surface acoustic wave (SAW) sensor, the piezoelectric material used in the fabrication of the sensor plays a crucial role in defining the response of the SAW sensor. As a ferroelectric material, barium strontium titanate (Ba0.6Sr0.4TiO3) has recently been studied due to its intriguing dielectric and electromechanical properties. Its high acoustic velocity and coupling coefficient make it a promising candidate for the development of acoustic devices; however, its use as a piezoelectric material in SAW sensors is still in its infancy. In this paper, we present the design, fabrication and validation of an indium doped SnO2-based SAW gas sensor on Ba0.6Sr0.4TiO3 thin film for room temperature (RT) applications. Pulsed laser deposition was used to deposit thin films of Ba0.6Sr0.4TiO3 and indium-doped SnO2. Different characterization techniques were employed to analyze the morphology and crystallization of the films. The performance of the fabricated sensor was validated by exposing it to different concentrations of ethanol and then analyzing the recorded frequency shift. The sensor exhibited fast response (39 s) and recovery (50 s) times with a sensitivity of 9.9 MHz/Δ. Moreover, the sensor had good linear response and reproducibility. The fabricated indium-doped SnO2-based SAW gas sensor could be suitable for practical room temperature applications. Full article
(This article belongs to the Section Inorganic Crystalline Materials)
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<p>Schematic representation of the fabrication process of a BST-based SAW gas sensor with In-doped SnO<sub>2</sub> sensing film.</p>
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<p>A microscopic picture of the fabricated SAW gas sensor.</p>
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<p>S<sub>21</sub> measurement of the BST based SAW sensor with Indium doped SnO<sub>2</sub> with a 2.5 µm of finger width and spacing of the IDT structures. The fundamental resonance was around 550 MHz. Higher order resonances can also be seen.</p>
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<p>Schematic illustration of ethanol vapor sensing measurement test setup. The flow rates were controlled using the two MFCs, and the sensor was mounted inside the gas chamber and connected to the network analyzer to record the data.</p>
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<p>XRD patterns of the BST films grown on silicon and sapphire substrates using PLD.</p>
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<p>SEM images of BST films deposited on different substrates: (<b>a</b>) top-view; (<b>b</b>) cross-sectional view of the BST film on Si.</p>
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<p>Dynamic response of the BST based SAW sensor with In-doped SnO<sub>2</sub> at different concentrations of ethanol (at flow rates ratio of 0.1, 0.2, 0.3 and 0.4) at room temperature.</p>
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<p>Fit for a plot of frequency shift versus concentration of ethanol.</p>
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<p>The reproducibility of the fabricated sensor at ethanol concentration of 0.3.</p>
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14 pages, 2524 KiB  
Article
Flame Spray Pyrolysis Synthesis of Vo-Rich Nano-SrTiO3-x
by Areti Zindrou, Pavlos Psathas and Yiannis Deligiannakis
Nanomaterials 2024, 14(4), 346; https://doi.org/10.3390/nano14040346 - 11 Feb 2024
Cited by 1 | Viewed by 1720
Abstract
Engineering of oxygen vacancies (Vo) in nanomaterials allows diligent control of their physicochemical properties. SrTiO3 possesses the typical ABO3 structure and has attracted considerable attention among the titanates due to its chemical stability and its high conduction band energy. This has [...] Read more.
Engineering of oxygen vacancies (Vo) in nanomaterials allows diligent control of their physicochemical properties. SrTiO3 possesses the typical ABO3 structure and has attracted considerable attention among the titanates due to its chemical stability and its high conduction band energy. This has resulted in its extensive use in photocatalytic energy-related processes, among others. Herein, we introduce the use of Flame Spray Pyrolysis (FSP); an industrial and scalable process to produce Vo-rich SrTiO3 perovskites. We present two types of Anoxic Flame Spray Pyrolysis (A-FSP) technologies using CH4 gas as a reducing source: Radial A-FSP (RA-FSP); and Axial A-FSP (AA-FSP). These are used for the control engineering of oxygen vacancies in the SrTiO3-x nanolattice. Based on X-ray photoelectron spectroscopy, Raman and thermogravimetry-differential thermal analysis, we discuss the role and the amount of the Vos in the so-produced nano-SrTiO3-x, correlating the properties of the nanolattice and energy-band structure of the SrTiO3-x. The present work further corroborates the versatility of FSP as a synthetic process and the potential future application of this process to engineer photocatalysts with oxygen vacancies in quantities that can be measured in kilograms. Full article
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Graphical abstract

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<p>(<b>A</b>) Schematic representation of Radial-CH<sub>4</sub> and (<b>B</b>) Axial-CH<sub>4</sub> A-FSP processes.</p>
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<p>(<b>A</b>) XRD patterns of the pristine and reduced STO nanomaterials. (<b>B</b>,<b>C</b>) Size distribution graphs obtained from several TEM images for STO-R5 and STO-A2 materials. (<span class="html-italic">Inset Figures:</span> TEM image of STO-R5 and STO-A2).</p>
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<p>(<b>A</b>) UV−Vis DRS absorption spectra of STO nanomaterials. (<b>B</b>) Tauc plots with the arrows pointing at the calculated Eg values of the STO nanomaterials. (<span class="html-italic">Top Figures:</span> Powder nanoparticles showcasing the color change).</p>
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<p>Raman spectra of the FSP−made STO nanomaterials, with the characteristic transverse optical band modes of TO<sub>1</sub>, TO<sub>2</sub>, TO<sub>3</sub>, and TO<sub>4</sub> and, additionally, the characteristic longitudinal optical band modes of LO<sub>2</sub> and LO<sub>4</sub>.</p>
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<p>(<b>A</b>) XPS measurements of the five materials for the fitted Ti 2<span class="html-italic">p</span><sub>1/2</sub> and Ti 2<span class="html-italic">p</span><sub>3/2</sub> XPS spectra; (<b>B</b>) oxygen XPS measurements of the five materials for the fitted lattice oxygen, oxygen vacancies, and surface oxygen-XPS spectra.</p>
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17 pages, 5305 KiB  
Article
PVA-Based Films with Strontium Titanate Nanoparticles Dedicated to Wound Dressing Application
by Beata Kaczmarek-Szczepańska, Lidia Zasada, Marcin Wekwejt, Maria Swiontek Brzezinska, Anna Michno, Anna Ronowska, Magdalena Ciesielska, Ganna Kovtun and M. Teresa Cuberes
Polymers 2024, 16(4), 484; https://doi.org/10.3390/polym16040484 - 9 Feb 2024
Cited by 1 | Viewed by 6009
Abstract
Bioactive materials may be applied in tissue regeneration, and an example of such materials are wound dressings, which are used to accelerate skin healing, especially after trauma. Here, we proposed a novel dressing enriched by a bioactive component. The aim of our study [...] Read more.
Bioactive materials may be applied in tissue regeneration, and an example of such materials are wound dressings, which are used to accelerate skin healing, especially after trauma. Here, we proposed a novel dressing enriched by a bioactive component. The aim of our study was to prepare and characterize poly(vinyl alcohol) films modified with strontium titanate nanoparticles. The physicochemical properties of films were studied, such as surface free energy and surface roughness, as well as the mechanical properties of materials. Moreover, different biological studies were carried out, like in vitro hemo- and cyto-compatibility, biocidal activity, and anti-biofilm formation. Also, the degradation of the materials’ utilization possibilities and enzymatic activity in compost were checked. The decrease of surface free energy, increase of roughness, and improvement of mechanical strength were found after the addition of nanoparticles. All developed films were cyto-compatible, and did not induce a hemolytic effect on the human erythrocytes. The PVA films containing the highest concentration of STO (20%) reduced the proliferation of Eschericha coli, Pseudomonas aeruginosa, and Staphylococcus aureus significantly. Also, all films were characterized by surface anti-biofilm activity, as they significantly lowered the bacterial biofilm abundance and its dehydrogenase activity. The films were degraded by the compost microorganism. However, PVA with the addition of 20%STO was more difficult to degrade. Based on our results, for wound dressing application, we suggest using bioactive films based on PVA + 20%STO, as they were characterized by high antibacterial properties, favorable physicochemical characteristics, and good biocompatibility with human cells. Full article
(This article belongs to the Section Biobased and Biodegradable Polymers)
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<p>(<b>A</b>) the Young Modulus (E<sub>mod</sub>), (<b>B</b>) maximum tensile strength (σ<sub>max</sub>) and (<b>C</b>) elongation at break (dl) determined for films based on PVA, PVA + 5%STO, PVA + 10%STO, and PVA + 20%STO. * significantly different from PVA (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>3D images of films surface (<b>A</b>) PVA; (<b>B</b>) PVA + 5%STO; (<b>C</b>) PVA + 10%STO; (<b>D</b>) PVA + 20%STO.</p>
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<p>The effect of developed films on cyto-compatibility of hFOB 1.19 cells (cell viability and lactate dehydrogenase release): (<b>a</b>) after 24 h and (<b>b</b>) after 72 h exposure to films extracts (n = 4; data are expressed as the mean ± SD, * statistical significance compared to the control–PVA (<span class="html-italic">p</span> &lt; 0.05)).</p>
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<p>The effect of developed films on hemo-compatibility of human erythrocytes (hemolysis rate and lactate dehydrogenase release) after 24 h exposure to films (n = 4, data are expressed as the mean ± SD, * significantly different from the negative control and <sup>#</sup> significantly different from the PVA (<span class="html-italic">p</span> &lt; 0.05)).</p>
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<p>Biocidal properties of PVA/STO films. Different letters over the bars indicate a significant difference between means (<span class="html-italic">p</span> &lt; 0.05).</p>
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<p>Biofilm abundance and respiratory activity on the surface of PVA/STO films. Columns were designated as biofilm and lines as dehydrogenase. Different letters over the bars indicate a significant difference between means (<span class="html-italic">p</span> &lt; 0.05), ±SD (n = 3).</p>
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<p>Biofilm abundance and respiratory activity on the surface of PVA/STO films. Columns were designated as biofilm and lines as dehydrogenase. Different letters over the bars indicate a significant difference between means (<span class="html-italic">p</span> &lt; 0.05), ±SD (n = 3).</p>
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<p>Biodegradation of PVA/STO as expressed in mgO<sub>2</sub>/kg compost. Different letters over the bars indicate a significant difference between means (<span class="html-italic">p</span> &lt; 0.05), ±SD (n = 3).</p>
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