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Search Results (397)

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Keywords = thermal storage devices

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13 pages, 6013 KiB  
Article
Development and Characterization of 3D-Printed PLA/Exfoliated Graphite Composites for Enhanced Electrochemical Performance in Energy Storage Applications
by Ananias Lima dos Santos, Francisco Cezar Ramos de Souza, João Carlos Martins da Costa, Daniel Araújo Gonçalves, Raimundo Ribeiro Passos and Leandro Aparecido Pocrifka
Polymers 2024, 16(22), 3131; https://doi.org/10.3390/polym16223131 - 9 Nov 2024
Viewed by 642
Abstract
This research introduces a new way to create a composite material (PLA/EG) for 3D printing. It combines polylactic acid (PLA) with exfoliated graphite (EG) using a physical mixing method, followed by direct mixing in a single-screw extruder. Structural and vibrational analyses using X-ray [...] Read more.
This research introduces a new way to create a composite material (PLA/EG) for 3D printing. It combines polylactic acid (PLA) with exfoliated graphite (EG) using a physical mixing method, followed by direct mixing in a single-screw extruder. Structural and vibrational analyses using X-ray diffraction and Fourier transform infrared spectroscopy confirmed the PLA/EG’s formation (composite). The analysis also suggests physical adsorption as the primary interaction between the two materials. The exfoliated graphite acts as a barrier (thermal behavior), reducing heat transfer via TG. Electrochemical measurements reveal redox activity (cyclic voltammetry) with a specific capacitance of ~ 6 F g−1, low solution resistance, and negligible charge transfer resistance, indicating ion movement through a Warburg diffusion process. Additionally, in terms of complex behavior (electrochemical impedance spectroscopy), the PLA/EG’s actual capacitance C’(ω) displayed a value greater than 1000 μF cm−2, highlighting the composite’s effectiveness in storing charge. These results demonstrate that PLA/EG composites hold significant promise as electrodes in electronic devices. The methodology used in this study not only provides a practical way to create functional composites but also opens doors for new applications in electronics and energy storage. Full article
(This article belongs to the Special Issue Advanced Analytical Methods for Applied Polymeric Science)
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Figure 1

Figure 1
<p>XRD standards of PLA, PLA/EG, and exfoliated graphite (EG).</p>
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<p>Bands observed in the FTIR spectra of PLA and PLA/EG.</p>
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<p>(<b>A</b>) Thermal behavior according to thermogravimetric analysis and (<b>B</b>) thermal behavior according to the thermogravimetric derivative.</p>
Full article ">Figure 3 Cont.
<p>(<b>A</b>) Thermal behavior according to thermogravimetric analysis and (<b>B</b>) thermal behavior according to the thermogravimetric derivative.</p>
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<p>Electrochemical behavior of PLA/EG according to cyclic voltammetry.</p>
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<p>Plots of peak currents vs. the square root of scan rate, with scan rates ranging from 1 to 100 mV s<sup>−1</sup>.</p>
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<p>(<b>A</b>) Electrochemical behavior according to EIS via Nyquist; (<b>B</b>) electrochemical behavior according to EIS via Bode; and (<b>C</b>) real part of the complex capacitance C’(ω) of PLA/EG.</p>
Full article ">Figure 6 Cont.
<p>(<b>A</b>) Electrochemical behavior according to EIS via Nyquist; (<b>B</b>) electrochemical behavior according to EIS via Bode; and (<b>C</b>) real part of the complex capacitance C’(ω) of PLA/EG.</p>
Full article ">Scheme 1
<p>Preparation and production of PLA/EG filaments via 3D printing.</p>
Full article ">
25 pages, 3366 KiB  
Review
An Overview of the R&D of Flywheel Energy Storage Technologies in China
by Xingjian Dai, Xiaoting Ma, Dongxu Hu, Jibing Duan and Haisheng Chen
Energies 2024, 17(22), 5531; https://doi.org/10.3390/en17225531 - 5 Nov 2024
Viewed by 524
Abstract
The literature written in Chinese mainly and in English with a small amount is reviewed to obtain the overall status of flywheel energy storage technologies in China. The theoretical exploration of flywheel energy storage (FES) started in the 1980s in China. The experimental [...] Read more.
The literature written in Chinese mainly and in English with a small amount is reviewed to obtain the overall status of flywheel energy storage technologies in China. The theoretical exploration of flywheel energy storage (FES) started in the 1980s in China. The experimental FES system and its components, such as the flywheel, motor/generator, bearing, and power electronic devices, were researched around thirty years ago. About twenty organizations devote themselves to the R&D of FES technology, which is developing from theoretical and laboratory research to the stage of engineering demonstration and commercial application. After the research and accumulation in the past 30 years, the initial FES products were developed by some companies around 10 years ago. Today, the overall technical level of China’s flywheel energy storage is no longer lagging behind that of Western advanced countries that started FES R&D in the 1970s. The reported maximum tip speed of the new 2D woven fabric composite flywheel arrived at 900 m/s in the spin test. A steel alloy flywheel with an energy storage capacity of 125 kWh and a composite flywheel with an energy storage capacity of 10 kWh have been successfully developed. Permanent magnet (PM) motors with power of 250–1000 kW were designed, manufactured, and tested in many FES assemblies. The lower loss is carried out through innovative stator and rotor configuration, optimizing magnetic flux and winding arrangement for harmonic magnetic field suppression. Permanent magnetic bearings with high load ability up to 50–100 kN were developed both for a 1000 kW/16.7 kWh flywheel used for the drilling practice application in hybrid power of an oil well drilling rig and for 630 kW/125 kWh flywheels used in the 22 MW flywheel array applied to the flywheel and thermal power joint frequency modulation demonstration project. It is expected that the FES demonstration application power stations with a total cumulative capacity of 300 MW will be built in the next five years. Full article
(This article belongs to the Section D: Energy Storage and Application)
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Figure 1

Figure 1
<p>Configuration of flywheel energy storage system.</p>
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<p>Six kinds of flywheel: (<b>a</b>) 1000 kWh flywheel concept design; (<b>b</b>) 200 Wh winding composite AMB flywheel; (<b>c</b>) woven fabric composite flywheel; (<b>d</b>) magnet element embedded fiber spoke flywheel; (<b>e</b>) 10 kWh composite flywheel (Tsinghua Univ.); and (<b>f</b>) 90 kWh steel flywheel (IET, CAS).</p>
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<p>A new type of M/G and flywheel. (<b>a</b>) The 3D model of the flywheel and M/G. (<b>b</b>) The profile view of the M/G.</p>
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<p>A 50–100 kN permanent magnetic bearing stator. (<b>a</b>) Permanent ring with sector blocks. (<b>b</b>) Halbach array magnetic ring.</p>
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<p>Charging and discharging principles of motor-power electronic system: (<b>a</b>) charging and (<b>b</b>) discharging.</p>
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<p>Charging and discharging principles of motor-power electronic system: (<b>a</b>) charging and (<b>b</b>) discharging.</p>
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<p>Integration flywheel energy storage system.</p>
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<p>Flywheel energy storage unit and array built in China: (<b>a</b>) 500 kw/50 kWh FESU, 2023, and (<b>b</b>) 20 MW Flywheels Array, 2023.</p>
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<p>Simulink model of the control of FES and wind power system.</p>
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<p>FES application in PV power.</p>
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<p>Potential energy regenerating and load leveling of oil drilling rig.</p>
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11 pages, 5820 KiB  
Article
Enhancing the Thermal Stability of Skyrmion in Magnetic Nanowires for Nanoscale Data Storage
by Mohammed Al Bahri, Mohammed Al Hinaai, Rayya Al Balushi and Salim Al-Kamiyani
Nanomaterials 2024, 14(21), 1763; https://doi.org/10.3390/nano14211763 - 3 Nov 2024
Viewed by 655
Abstract
Magnetic skyrmion random switching and structural stability are critical limitations for storage data applications. Enhancing skyrmions’ magnetic properties could improve their thermal structural stability. Hence, micromagnetic calculation was carried out to explore the thermal nucleation and stability of skyrmions in magnetic nanodevices. Different [...] Read more.
Magnetic skyrmion random switching and structural stability are critical limitations for storage data applications. Enhancing skyrmions’ magnetic properties could improve their thermal structural stability. Hence, micromagnetic calculation was carried out to explore the thermal nucleation and stability of skyrmions in magnetic nanodevices. Different magnetic properties such as uniaxial magnetic anisotropy energy (Ku), saturation magnetization (Ms) and Dzyaloshinskii—Moriya interaction (DMI) were used to assess the thermal stability of skyrmions in magnetic nanowires. For some values of Ms and Ku, the results verified that the skyrmion structure is stable at temperatures above 800 K, which is higher than room temperature. Additionally, manipulating the nanowire geometry was found to have a substantial effect on the thermal structural stability of the skyrmion in storage nanodevices. Increasing the nanowire dimensions, such as length or width, enhanced skyrmions’ structural stability against temperature fluctuations in nanodevices. Furthermore, the random nucleation of the skyrmions due to the device temperature was examined. It was shown that random skyrmion nucleation occurs at temperature values greater than 700 K. These findings make skyrmion devices suitable for storage applications. Full article
(This article belongs to the Special Issue Magnetism and Spintronics at the Nanoscale)
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Figure 1

Figure 1
<p>(<b>a</b>). The skyrmion (radius of 50 nm) at a device (200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>)</mo> </mrow> </semantics></math> temperature of 0 K. The magnetization aligns in the negative z-direction in the initial state can be seen (blue) and in the positive z-direction (red). (<b>b</b>). The skyrmion under a temperature of 100 K in a nanowire with dimensions of (200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>)</mo> </mrow> </semantics></math>.</p>
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<p>(<b>a</b>) The skyrmion at 0 K with a radius of 50 nm and magnetization aligned along the positive <span class="html-italic">z</span>-axis (red) at t = 0 ns. (<b>b</b>) The skyrmion under a temperature of 0 K reaches the end of a nanowire with dimensions (200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>)</mo> </mrow> </semantics></math>. The magnetic properties are <span class="html-italic">Ku</span> = 0.5 <math display="inline"><semantics> <mrow> <mo> </mo> <mo>×</mo> <mo> </mo> </mrow> </semantics></math> 10<sup>5</sup> Jm<sup>−3</sup> and <math display="inline"><semantics> <mrow> <mi>M</mi> <mi>s</mi> <mo>=</mo> <mn>1.0</mn> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>6</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo>.</mo> </mrow> </semantics></math> (<b>c</b>) Normalized <span class="html-italic">m<sub>z</sub></span> versus time in a magnetic nanowire under two values of current density.</p>
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<p>Skyrmion in a device with dimensions of 200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math> at a temperature of 150 K after (<b>a</b>) 0.65 ns, (<b>b</b>) 2.27 ns, (<b>c</b>) 2.50 ns, (<b>d</b>) 3.1 ns. (<b>e</b>) The skyrmion completely annihilates at a device temperature of 150 K after 4 ns. The magnetic properties are <span class="html-italic">Ku</span> = 0.5 <math display="inline"><semantics> <mrow> <mo> </mo> <mo>×</mo> <mo> </mo> </mrow> </semantics></math> 10<sup>5</sup> Jm<sup>−3</sup> and <math display="inline"><semantics> <mrow> <mi>M</mi> <mi>s</mi> <mo>=</mo> <mn>1.0</mn> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>6</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> </semantics></math>.</p>
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<p>(<b>a</b>) Skyrmion annihilation temperature versus current density for skyrmion radii of 30 nm and 50 nm. (<b>b</b>) Skyrmion motion to the right in magnetic nanowire under a specific value of current density. (<b>c</b>) Skyrmion propagation under <math display="inline"><semantics> <mrow> <mi>J</mi> <mo>=</mo> <mn>1.2</mn> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>12</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>2</mn> </mrow> </msup> </mrow> </semantics></math> at a device’s temperature of 100 K. (<b>d</b>) Skyrmion propagation under <math display="inline"><semantics> <mrow> <mi>J</mi> <mo>=</mo> <mn>1.2</mn> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>12</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>2</mn> </mrow> </msup> </mrow> </semantics></math> at a device’s temperature of 150 K. The magnetic properties are <math display="inline"><semantics> <mrow> <mi>M</mi> <mi>s</mi> <mo>=</mo> <mn>1.5</mn> <mo> </mo> <mo> </mo> <mo>×</mo> <mo> </mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>6</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> </semantics></math> and <span class="html-italic">Ku</span> = 0.5 × 10<sup>5</sup> Jm<sup>−3</sup>. The nanowire dimensions are 200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>.</p>
Full article ">Figure 5
<p>Graph of skyrmion stability time (<span class="html-italic">r</span> = 50 nm) versus device temperature in nanowires (200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>)</mo> </mrow> </semantics></math> for three values of (<b>a</b>) <span class="html-italic">Ku</span> and (<b>b</b>) <span class="html-italic">Ms</span>.</p>
Full article ">Figure 6
<p>Skyrmion annihilation temperature versus <span class="html-italic">Ms</span> for skyrmion radii of 30 nm and 50 nm: (<b>a</b>) and <span class="html-italic">Ku</span> (<b>b</b>). The current density used is <math display="inline"><semantics> <mrow> <mi>J</mi> <mo>=</mo> <mn>2.5</mn> <mo> </mo> <mo> </mo> <mo>×</mo> <mo> </mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>11</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>2</mn> </mrow> </msup> </mrow> </semantics></math>, and the nanowire dimensions are 200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>.</p>
Full article ">Figure 7
<p>Plots of skyrmion stability time versus DMI for device temperatures of 100 K, 200 K and 300 K under <span class="html-italic">J</span> = 2.5 × 10<sup>11</sup> Am<sup>−2</sup>, <span class="html-italic">Ku</span> = 0.5 × 10<sup>5</sup> Jm<sup>−3</sup> and <math display="inline"><semantics> <mrow> <mi>M</mi> <mi>s</mi> <mo>=</mo> <mn>1.5</mn> <mo> </mo> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>6</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> </semantics></math>. The skyrmion (r = 50 nm) is in a nanowire with 200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>.</p>
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<p>Plots of skyrmion (<span class="html-italic">r</span> = 50 nm) stability time in nanowires versus (<b>a</b>) device width (<span class="html-italic">w</span>) and (<b>b</b>) device length (<span class="html-italic">L</span>) for a range of temperatures (100 K, 200 K and 300 K). The current density used is <span class="html-italic">J</span> = 2.5 × 10<sup>11</sup> Am<sup>−2</sup>, <math display="inline"><semantics> <mrow> <mi>M</mi> <mi>s</mi> <mo>=</mo> <mn>1.5</mn> <mo> </mo> <mo> </mo> <mo>×</mo> <mo> </mo> <msup> <mrow> <mn>10</mn> </mrow> <mrow> <mn>6</mn> </mrow> </msup> <mo> </mo> <mi mathvariant="normal">A</mi> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> </semantics></math> and <span class="html-italic">Ku</span> = 0.5 × 10<sup>5</sup> Jm<sup>−3</sup>.</p>
Full article ">Figure 9
<p>Plots of skyrmion stability time in nanowires versus (a) device thickness (th) for two device temperatures (100 K and 200 K). Nanowire dimensions are 200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> </mrow> </semantics></math>.</p>
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<p>(<b>a</b>) Random thermal creation of a skyrmion in a nanowire (200 <math display="inline"><semantics> <mrow> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>40</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo> </mo> <mo>×</mo> <mo> </mo> <mn>3</mn> <mo> </mo> <mi mathvariant="normal">n</mi> <mi mathvariant="normal">m</mi> <mo>)</mo> </mrow> </semantics></math> under a device temperature of 700 K. (<b>b</b>) Plot of skyrmion creation temperature against <span class="html-italic">Ms</span> for two current density values.</p>
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12 pages, 4492 KiB  
Article
Evaluation of Thermal and Mechanical Properties of Bi-In-Sn/WO3 Composites for Efficient Heat Dissipation
by Die Wu, Zhen Ning, Yanlin Zhu and Rui Yuan
Materials 2024, 17(21), 5315; https://doi.org/10.3390/ma17215315 - 31 Oct 2024
Viewed by 493
Abstract
Phase change materials (PCMs) offer promising solutions for efficient thermal management in electronic devices, energy storage systems, and renewable energy applications due to their capacity to store and release significant thermal energy during phase transitions. This study investigates the thermal and physical properties [...] Read more.
Phase change materials (PCMs) offer promising solutions for efficient thermal management in electronic devices, energy storage systems, and renewable energy applications due to their capacity to store and release significant thermal energy during phase transitions. This study investigates the thermal and physical properties of Bi-In-Sn/WO3 composites, specifically for their use as phase change thermal interface materials (PCM-TIMs). The Bi-In-Sn/WO3 composite was synthesized through mechanochemical grinding, which enabled the uniform dispersion of WO3 particles within the Bi-In-Sn alloy matrix. The addition of WO3 particles markedly improved the composite’s thermal conductivity and transformed its physical form into a putty-like consistency, addressing leakage issues typically associated with pure Bi-In-Sn alloys. Microstructural analyses demonstrated the existence of a continuous interface between the liquid metal and WO3 phases, with no gaps, ensuring structural stability. Thermal performance tests demonstrated that the Bi-In-Sn/WO3 composite achieved improved thermal conductivity, and reduced volumetric latent heat, and there was a slight increase in thermal contact resistance with higher WO3 content. These findings highlight the potential of Bi-In-Sn/WO3 composites for utilization as advanced PCM-TIMs, offering enhanced heat dissipation, stability, and physical integrity for high-performance electronic and energy systems. Full article
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Figure 1

Figure 1
<p>Schematic illustration of synthesis and microstructure of Bi-In-Sn/WO<sub>3</sub> composite via mechanochemistry. (<b>a</b>) Mechanochemical process between LM (Bi-In-Sn) and WO<sub>3</sub> particles; (<b>b</b>) Normal composites showing gaps at the interface between LM and WO<sub>3</sub> phases; (<b>c</b>) Our Bi-In-Sn/WO<sub>3</sub> composite showing a continuous, gap-free interface. Note: Color-coded elements include W (blue), O (light blue), Ga (green), In (yellow), and Sn (orange). Arrows indicate the direction of atomic interaction under shear.</p>
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<p>SEM image of Bi-In-Sn/WO<sub>3</sub> composite. The red-highlighted areas represent tungsten (W) distribution in the composite.</p>
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<p>Optical images of (<b>a</b>) pure Bi-In-Sn; and (<b>b</b>) Bi-In-Sn/WO<sub>3</sub> composite.</p>
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<p>X-ray diffractogram of Bi-In-Sn/WO<sub>3</sub> composite.</p>
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<p>XPS analysis of (<b>a</b>) WO<sub>3</sub>, and (<b>b</b>) Bi-In-Sn/WO<sub>3</sub> composite.</p>
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<p>(<b>a</b>) A schematic representation of the Bi-In-Sn/WO<sub>3</sub> composite following FIB cutting and HADDF imaging, with the arrow indicating the direction of the line scan; (<b>b</b>) EDS line scan showing the distribution of O, W, Bi, In, and Sn along the interface.</p>
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<p>(<b>a</b>) High-resolution transmission electron microscopy image of Bi-In-Sn/WO<sub>3</sub> interface, showing lattice structure. The green box highlights the Bi-In-Sn region, while the yellow box marks the transition interface with WO<sub>3</sub>; (<b>b</b>) SAED pattern of Bi-In-Sn (green box); and (<b>c</b>) transition interface between Bi-In-Sn and WO<sub>3</sub> (yellow box).</p>
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<p>Thermal conductivity of Bi-In-Sn/WO<sub>3</sub> composite as function of WO<sub>3</sub> mass fraction.</p>
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<p>Thermal contact resistance of Bi-In-Sn/WO<sub>3</sub> composite as function of WO<sub>3</sub> mass fraction.</p>
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<p>Volumetric latent heat of Bi-In-Sn/WO<sub>3</sub> composite as function of WO<sub>3</sub> mass fraction.</p>
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<p>Phase transition temperature (T<sub>m</sub>) of Bi-In-Sn/WO<sub>3</sub> composite as function of WO<sub>3</sub> mass fraction.</p>
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18 pages, 3192 KiB  
Article
The Influence of Thermal Treatment of Activated Carbon on Its Electrochemical, Corrosion, and Adsorption Characteristics
by Andrzej Świątkowski, Elżbieta Kuśmierek, Krzysztof Kuśmierek and Stanisław Błażewicz
Molecules 2024, 29(20), 4930; https://doi.org/10.3390/molecules29204930 - 18 Oct 2024
Viewed by 429
Abstract
Activated carbons can be applied in various areas of our daily life depending on their properties. This study was conducted to investigate the effect of thermal treatment of activated carbon on its properties, considering its future use. The characteristics of activated carbon heat-treated [...] Read more.
Activated carbons can be applied in various areas of our daily life depending on their properties. This study was conducted to investigate the effect of thermal treatment of activated carbon on its properties, considering its future use. The characteristics of activated carbon heat-treated at temperatures of 1500, 1800, and 2100 °C based on its future use are presented. The significant effect of the treatment temperature on morphological, adsorption, electrochemical, and corrosion properties was proved. Increasing the temperature above 1800 °C resulted in a significant decrease in the specific surface area (from 969 to 8 m2·g−1) and material porosity—the formation of mesopores (20–100 nm diameter) was observed. Simultaneously, adsorption capability, double layer capacity, and electrochemically active surface area also decreased, which helped to explain the shape of cyclic voltammograms recorded in 2,4-dichlorophenoxyacetic acid and in supporting electrolytes. However, a significant increase in corrosion resistance was found for the carbon material treated at a temperature of 2100 °C (corrosion current decreased by 23 times). Comparison of morphological, adsorption, corrosion, and electrochemical characteristics of the tested activated carbon, its applicability as an electrode material in electrical energy storage devices, and materials for adsorptive removal of organic compounds from wastewater or as a sensor in electrochemical determination of organic compounds was discussed. Full article
(This article belongs to the Special Issue Exclusive Feature Papers in Electrochemistry)
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<p>SEM images of the activated carbon samples (AC1500, AC1800 and AC2100) recorded at magnifications of 500 (<b>top</b>) and 2000 (<b>bottom</b>).</p>
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<p>Nitrogen adsorption–desorption isotherms (<b>left side</b>) and pore size distribution dV/dD plots (<b>right side</b>) determined for the activated carbon samples.</p>
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<p>Adsorption isotherms of 2,4-D from 0.1 mol·L<sup>−1</sup> KCl onto activated carbons (line: fitting of Langmuir model). Experimental conditions: 2,4-D initial concentrations = 0.3–1.0 mmol·L<sup>−1</sup>, activated carbon dosage = 0.5 g·L<sup>−1</sup>, temperature = 23 °C, pH = native (original).</p>
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<p>Potentiodynamic polarization curves recorded for the activated carbon samples in KCl solution (0.1·mol L<sup>−1</sup>).</p>
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<p>Exemplary potentiodynamic polarization curves recorded for AC1800 material in 0.1 mol·L<sup>−1</sup> KCl in three consecutive measurements.</p>
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<p>Cyclic voltammograms recorded on activated carbon samples in a 0.001 mol·L<sup>−1</sup> 2,4-D solution (0.1 mol·L<sup>−1</sup> KCl); v = 20 mV·s<sup>−1</sup>, AC1500 and AC1800 (left axis); AC2100 (right axis).</p>
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<p>Cyclic voltammograms recorded in 0.1 mol·L<sup>−1</sup> KCl for AC1500 (left axis), AC1800 (left axis), and AC2100 (right axis) carbon materials; v = 10 mV·s<sup>−1</sup>.</p>
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<p>Dependences <span class="html-italic">1/q*</span> vs. <span class="html-italic">v</span><sup>1/2</sup> (<b>A</b>) and <span class="html-italic">q*</span> vs. <span class="html-italic">v</span><sup>−1/2</sup> (<b>B</b>) determined for the activated carbons in KCl solution. AC1500 and AC1800—left axis, AC2100—right axis.</p>
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21 pages, 4261 KiB  
Article
The Study of an Improved Particle Swarm Optimization Algorithm Applied to Economic Dispatch in Microgrids
by Ang Dong and Seon-Keun Lee
Electronics 2024, 13(20), 4086; https://doi.org/10.3390/electronics13204086 - 17 Oct 2024
Viewed by 507
Abstract
With the widespread use of fossil fuels, the Earth’s environment is facing a severe threat of degradation. Traditional large-scale power grids have struggled to meet the ever-growing demands of modern society. The implementation and functioning of microgrids not only enhance the use of [...] Read more.
With the widespread use of fossil fuels, the Earth’s environment is facing a severe threat of degradation. Traditional large-scale power grids have struggled to meet the ever-growing demands of modern society. The implementation and functioning of microgrids not only enhance the use of renewable energy sources but also considerably diminish the environmental damage resulting from fossil fuel consumption. However, the inherent instability of renewable energy presents a major challenge to the reliability of microgrids. To address the uncertainties of wind and photovoltaic power generation, it is urgent to adopt effective operational control methods to adjust power distribution, thereby achieving an economically efficient system operation and ensuring a reliable power supply. This paper utilizes a microgrid system consisting of wind power, photovoltaic power generation, thermal power units, and energy storage devices as the research object, establishing an economic dispatch model aimed at minimizing the total operating cost of the system. To solve this problem, the paper introduces second-order oscillatory particles and improves the Particle Swarm Optimization algorithm, proposing a second-order oscillatory chaotic mapping particle swarm optimization (SCMPSO). The simulation results show that this method can effectively optimize system operating costs while ensuring the stable operation of the microgrid. Full article
(This article belongs to the Topic Advances in Power Science and Technology, 2nd Edition)
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<p>Optimized scheduling flowchart.</p>
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<p>Learning factor iteration graph.</p>
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<p>Oscillation convergence curve.</p>
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<p>Progressive convergence curve.</p>
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<p>Test results of each benchmark function.</p>
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<p>Iteration comparison of different Particle Swarm Optimization algorithms.</p>
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<p>Algorithm Flowchart.</p>
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<p>Multi-source microgrid structure.</p>
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<p>Daily load data diagram.</p>
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<p>Typical summer wind speed.</p>
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<p>Typical summer 24-h temperature.</p>
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<p>Measurement of 24-h solar irradiance intensity.</p>
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<p>Image of 24-h power curves of distributed energy sources and energy storage devices.</p>
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<p>Diagram of electricity purchase and sale between microgrid and main grid system.</p>
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13 pages, 5155 KiB  
Article
Electronic, Optical and Thermoelectric Properties of Two-Dimensional Molybdenum Carbon Mo2C-MXenes
by Doan Thi Kieu Anh, Pham Hong Minh, Kohei Yamanoi, Marilou Cadatal-Raduban, Luong Viet Mui, Do Minh Hieu and Nguyen Dai Hung
Appl. Sci. 2024, 14(20), 9257; https://doi.org/10.3390/app14209257 - 11 Oct 2024
Viewed by 598
Abstract
We investigate the structural, electronic, optical, and thermoelectric properties of three compositions of Mo2C-MXenes (Mo2CF2, Mo2C(OH)2, and Mo2CO2) from monolayer to multilayer by first principles calculation within Density Functional [...] Read more.
We investigate the structural, electronic, optical, and thermoelectric properties of three compositions of Mo2C-MXenes (Mo2CF2, Mo2C(OH)2, and Mo2CO2) from monolayer to multilayer by first principles calculation within Density Functional Theory (DFT) and Boltzmann transport theory. Firstly, the atomic structures of Mo2C-MXenes are optimized, and their respective structures are created with comparative research. Secondly, their electronic band structures and optical properties are studied in detail. The estimation of the bandgap energy of Mo2C-MXenes with its functionalization reveal that most Mo2CF2 and Mo2C(OH)2 layers are semiconductors, while Mo2CO2 behaves as a metal. The electrical and optical properties can be altered by controlling the on-surface functional groups and the number of layers. Computation of the thermoelectric (TE) properties of Mo2C-MXenes reveals that, upon heating to 600 K, Mo2CF2 and Mo2C(OH)2 exhibit a high Seebeck coefficient and a relatively high electrical conductivity. The Seebeck coefficient reaches ~400 µV K−1 at room temperature for all layers of Mo2CF2 MXenes. Our results prove that Mo2CF2 is considered a promising material for thermoelectric devices, while Mo2CO2 does not possess better thermoelectric performance. Mo2C-MXenes from monolayer to multilayer have outstanding properties, such as flexible bandgap energy and high thermal stability, making them promising candidates for many applications, including energy storage and electrode applications. Full article
(This article belongs to the Special Issue Optical Materials, Structures, and Devices)
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<p>Structure of monolayer and multilayer for Mo<sub>2</sub>CF<sub>2</sub> (<b>a</b>), Mo<sub>2</sub>C(OH)<sub>2</sub> (<b>b</b>), and Mo<sub>2</sub>CO<sub>2</sub> (<b>c</b>) MXenes.</p>
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<p>Electronic band structures of monolayer and multilayer for Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub>, and Mo<sub>2</sub>CO<sub>2</sub> MXenes.</p>
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<p>Total and partial density of states for 2D layered Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub> and Mo<sub>2</sub>CO<sub>2</sub>.</p>
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<p>Real part and imaginary part of the dielectric function of monolayer and multilayer for Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub>, and Mo<sub>2</sub>CO<sub>2</sub>.</p>
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<p>Seebeck coefficient as a function of the chemical potential for monolayer and multilayer at different temperatures for Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub>, and Mo<sub>2</sub>CO<sub>2</sub>.</p>
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<p>Electrical conductivity as a function of the chemical potential at different temperatures from 300 K to 600 K for monolayer and multilayer Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub>, and Mo<sub>2</sub>CO<sub>2</sub>, respectively.</p>
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<p>Electronic thermal conductivity of Mo<sub>2</sub>CF<sub>2</sub>, Mo<sub>2</sub>C(OH)<sub>2</sub>, and Mo<sub>2</sub>CO<sub>2</sub> monolayer and multilayer structures as a function of chemical potential at different temperatures from 300–600 K.</p>
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20 pages, 5493 KiB  
Article
Exploring the Application of Advanced Chromatographic Methods to Characterize the Surface Physicochemical Properties and Transition Phenomena of Polystyrene-b-poly(4-vinylpyridine)
by Tayssir Hamieh
Molecules 2024, 29(20), 4812; https://doi.org/10.3390/molecules29204812 - 11 Oct 2024
Viewed by 697
Abstract
The linear diblock copolymer polystyrene-b-poly(4-vinylpyridine) (PS-P4VP) is an important copolymer recently used in many applications such as optoelectronics, sensors, catalysis, membranes, energy conversion, energy storage devices, photolithography, and biomedical applications. (1) Background: The surface thermodynamic properties of PS-P4VP copolymers are of [...] Read more.
The linear diblock copolymer polystyrene-b-poly(4-vinylpyridine) (PS-P4VP) is an important copolymer recently used in many applications such as optoelectronics, sensors, catalysis, membranes, energy conversion, energy storage devices, photolithography, and biomedical applications. (1) Background: The surface thermodynamic properties of PS-P4VP copolymers are of great importance in many chemical and industrial processes. (2) Methods: The inverse gas chromatography (IGC) at infinite dilution was used for the experimental determination of the retention volumes of organic solvents adsorbed on copolymer surfaces as a function of temperature. This led to the variations in the free energy of interaction necessary to the evaluation of the London dispersive and polar acid–base surface energies, the polar enthalpy and entropy, the Lewis acid–base constants, and the transition temperatures of the PS-P4VP copolymer. (3) Results: The application of the thermal Hamieh model led to an accurate determination of the London dispersive surface energy of the copolymer that showed non-linear variations versus the temperature, highlighting the presence of two transition temperatures. It was observed that the Lewis acid–base parameters of the copolymer strongly depend on the temperature, and the Lewis base constant of the solid surface was shown to be higher than its acid constant. (4) Conclusions: An important effect of the temperature on the surface thermodynamic properties of PS-P4VP was proven and new surface correlations were determined. Full article
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Graphical abstract

Graphical abstract
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<p>Variations in <math display="inline"><semantics> <mrow> <mi>R</mi> <mi>T</mi> <mi>l</mi> <mi>n</mi> <mi>V</mi> <mi>n</mi> </mrow> </semantics></math> (kJ/mol) of n-alkanes and polar solvents adsorbed on the PS-<span class="html-italic">b-</span>P4VP diblock copolymer as a function of temperature.</p>
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<p>Variations in the London dispersive surface energy <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mi>d</mi> </mrow> </msubsup> <mo> </mo> <mo>(</mo> <mi mathvariant="normal">m</mi> <mi mathvariant="normal">J</mi> <mo>/</mo> <msup> <mrow> <mi mathvariant="normal">m</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msup> <mo>)</mo> </mrow> </semantics></math> of the PS<span class="html-italic">-b-</span>P4VP diblock copolymer as a function of the temperature <span class="html-italic">T</span> (K) using the Hamieh thermal model. The vertical red arrows indicate the transition temperatures of the copolymer.</p>
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<p>Evolution of polar free interaction energy <math display="inline"><semantics> <mrow> <mo>(</mo> <mo>−</mo> <mo>∆</mo> <msubsup> <mrow> <mi>G</mi> </mrow> <mrow> <mi>a</mi> </mrow> <mrow> <mi>p</mi> </mrow> </msubsup> <mfenced separators="|"> <mrow> <mi>T</mi> </mrow> </mfenced> <mo>)</mo> </mrow> </semantics></math> (kJ/mol) of different polar solvents adsorbed on PS<span class="html-italic">-b-</span>P4VP diblock copolymer.</p>
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<p>Variations in the polar interaction enthalpy <math display="inline"><semantics> <mrow> <mo>(</mo> <mo>−</mo> <mo>∆</mo> <msubsup> <mrow> <mi>H</mi> </mrow> <mrow> <mi>a</mi> </mrow> <mrow> <mi>p</mi> </mrow> </msubsup> <mfenced separators="|"> <mrow> <mi>T</mi> </mrow> </mfenced> <mo> </mo> <mo>(</mo> <mi mathvariant="normal">k</mi> <mi mathvariant="normal">J</mi> <mo>/</mo> <mi mathvariant="normal">m</mi> <mi mathvariant="normal">o</mi> <mi mathvariant="normal">l</mi> <mo>)</mo> </mrow> </semantics></math> (<b>a</b>) and entropy (<math display="inline"><semantics> <mrow> <mo>−</mo> <mo>∆</mo> <msubsup> <mrow> <mi>S</mi> </mrow> <mrow> <mi>a</mi> </mrow> <mrow> <mi>p</mi> </mrow> </msubsup> <mfenced separators="|"> <mrow> <mi>T</mi> <mo>)</mo> </mrow> </mfenced> <mo> </mo> <mo>(</mo> <mi mathvariant="normal">J</mi> <msup> <mrow> <mi mathvariant="normal">K</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <msup> <mrow> <mi mathvariant="normal">m</mi> <mi mathvariant="normal">o</mi> <mi mathvariant="normal">l</mi> </mrow> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo>)</mo> </mrow> </semantics></math> (<b>b</b>) of polar solvents adsorbed on the PS-<span class="html-italic">b</span>-P4VP diblock copolymer.</p>
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<p>Variations in the various enthalpic and entropic acid–base parameters of the PS<span class="html-italic">-b-</span>P4VP diblock copolymer as a function of the temperature—(<b>a</b>): <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> </mrow> </semantics></math>, (<b>b</b>): <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> </mrow> </semantics></math>, (<b>c</b>): <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> </mrow> </semantics></math><span class="html-italic">/</span><math display="inline"><semantics> <mrow> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <mo>(</mo> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> <mo>+</mo> <msub> <mrow> <mi>K</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> <mo>)</mo> </mrow> </semantics></math>, (<b>d</b>): <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> <mo> </mo> </mrow> </semantics></math><span class="html-italic">/</span><math display="inline"><semantics> <mrow> <msub> <mrow> <mo> </mo> <mi>ω</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mrow> <mo>(</mo> <mi>ω</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> <mo>+</mo> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> <mo>)</mo> </mrow> </semantics></math>. The values of <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>A</mi> </mrow> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>ω</mi> </mrow> <mrow> <mi>D</mi> </mrow> </msub> </mrow> </semantics></math> given in the figures were multiplied by 10<sup>3</sup>.</p>
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<p>Variations in the separation distance <span class="html-italic">H</span> (<span class="html-italic">T</span>) (Å) of the PS<span class="html-italic">-b-</span>P4VP diblock copolymer as a function of the temperature <span class="html-italic">T</span> (K).</p>
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<p>Evolutions of the different components of surface energies <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mo>+</mo> </mrow> </msubsup> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mo>−</mo> </mrow> </msubsup> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mi>p</mi> </mrow> </msubsup> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mi>d</mi> </mrow> </msubsup> </mrow> </semantics></math>, and <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>s</mi> </mrow> <mrow> <mi>t</mi> <mi>o</mi> <mi>t</mi> <mo>.</mo> </mrow> </msubsup> </mrow> </semantics></math> (mJ/m<sup>2</sup>) of the PS<span class="html-italic">-b-</span>P4VP diblock copolymer as a function of the temperature.</p>
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<p>Variations in the polar component of the surface energy <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>γ</mi> </mrow> <mrow> <mi>l</mi> </mrow> <mrow> <mi mathvariant="normal">p</mi> </mrow> </msubsup> <mo>(</mo> <mi>T</mi> <mo>)</mo> </mrow> </semantics></math> (mJ/m<sup>2</sup>) of the different polar solvents adsorbed on the PS-<span class="html-italic">b</span>-P4VP diblock copolymer as a function of the temperature.</p>
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<p>Evolution of <math display="inline"><semantics> <mrow> <msubsup> <mrow> <mi>W</mi> </mrow> <mrow> <mi>a</mi> </mrow> <mrow> <mi>p</mi> </mrow> </msubsup> <mfenced separators="|"> <mrow> <mi>C</mi> <mi>o</mi> <mi>p</mi> <mi>o</mi> <mi>l</mi> <mi>y</mi> <mi>m</mi> <mi>e</mi> <mi>r</mi> <mo>−</mo> <mi>X</mi> </mrow> </mfenced> </mrow> </semantics></math> (mJ/m<sup>2</sup>) of polar molecules adsorbed on PS<span class="html-italic">-b-</span>P4VP copolymer.</p>
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17 pages, 4775 KiB  
Article
Performance of Protection Devices Integrated into Lithium-Ion Cells during Overcharge Abuse Test
by Carla Menale, Francesco Vitiello, Antonio Nicolò Mancino, Antonio Scotini, Livia Della Seta, Francesco Vellucci and Roberto Bubbico
Energies 2024, 17(19), 4785; https://doi.org/10.3390/en17194785 - 25 Sep 2024
Viewed by 645
Abstract
Lithium-ion batteries currently represent the most suitable technology for energy storage in various applications, such as hybrid and electric vehicles (HEVs and BEVs), portable electronics and energy storage systems. Their wide adoption in recent years is due to their characteristics of high energy [...] Read more.
Lithium-ion batteries currently represent the most suitable technology for energy storage in various applications, such as hybrid and electric vehicles (HEVs and BEVs), portable electronics and energy storage systems. Their wide adoption in recent years is due to their characteristics of high energy density, high power density and long life cycle. On the other hand, they still face challenges from a safety point of view for the possible faults that could generate several problems, ranging from simple malfunctioning to a dangerous thermal runaway. Overcharge is one of the most critical types of faults, and, depending on the level of abuse, it may trigger a thermal runaway. To prevent high levels of overcharge abuse, some cells include integrated protection devices that cut off the circuit when a critical condition is met. In this paper, the performance of these protection devices is evaluated to assess their effectiveness. The cells were tested at different ambient temperatures and current levels. In the worst-case scenarios, the maximum cell temperature slightly exceeded 70 °C and the State of Charge (SOC) reached a peak of 127% when the Current Interruption Device (CID) was activated. These conditions were not critical, so serious events such as thermal runaway were not triggered. These outcomes confirm the effectiveness of the CID, which always intervenes in maintaining a safe state. However, since it never intervened in the overcharge abuse tests, a specific set up was also used to investigate the operation of the other protection device, the Positive Temperature Coefficient. Full article
(This article belongs to the Special Issue Current Advances in Fuel Cell and Batteries)
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<p>(<b>a</b>) FARO Plant with equipment: 1—bulletproof box with cell set up; 2—fire extinguishers; 3—PC; 4—thermal infrared camera: FIir S60; 5—fast camera: Redlake MotionPro Y3S1-M; 6—Eltra E-8325 portable cycler. (<b>b</b>) Detail of set up inside bulletproof box: 1—cell under test; 2—thermocouples.</p>
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<p>Climate chamber for abuse tests: (<b>a</b>) outside (<b>b</b>) inside.</p>
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<p>Case for abuse tests: (<b>a</b>) preliminary design drawings; (<b>b</b>) implementation: 1—polycarbonate tube with closing plates; 2—pressure transducer; 3—safety valve; 4—drain valve.</p>
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<p>Disassembled cell: (<b>a</b>) separator (<b>b</b>) cathode.</p>
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<p>Unprotected cells. Overcharge test with a constant current of 9.6 A (3C) in open air: (<b>a</b>) temperature difference and current of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Unprotected cells. Overcharge test with a constant current of 3.2 A (1C) in open air: (<b>a</b>) temperature difference and current of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Unprotected cells. Overcharge test with a constant current of 1.6 A (0.5C) in open air: (<b>a</b>) temperature difference and current of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Thermal image of the overcharge test with a constant current of 9.6 A (3C) in open air after: (<b>a</b>) t = 27 s; (<b>b</b>) t = 149 s; (<b>c</b>) t = 230 s [<a href="#B24-energies-17-04785" class="html-bibr">24</a>].</p>
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<p>Unprotected cells. Overcharge tests with a constant current of 9.6 A (3C) at different initial temperatures: temperature at the positive connector and current of the abused cells.</p>
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<p>Unprotected cells. Overcharge test with a constant current of 9.6 A (3C) at 50 °C ambient temperature: (<b>a</b>) temperature and current of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Protected cells. Overcharge test with a target current of 9.6 A (3C) in open air: (<b>a</b>) temperature and voltage of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Protected cells. Overcharge test with a target current of 3.2 A (1C) in open air: (<b>a</b>) temperature and voltage of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>Protected cells. Overcharge test with a target current of 3.2 A (1C) in open air after discharge at 80% SOC: (<b>a</b>) temperature and voltage of the abused cell; (<b>b</b>) voltage and current of the abused cell.</p>
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<p>SEM at 500× with Secondary and Backscattering Electrons (SE/BSE) of the anode: (<b>a</b>) new cell; (<b>b</b>) abused cell.</p>
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<p>SEM at 5k× with Secondary and Backscattering Electrons (SE/BSE) of the anode: (<b>a</b>) new cell; (<b>b</b>) abused cell.</p>
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<p>SEM at 500× with Secondary and Backscattering Electrons (SE/BSE) of the cathode: (<b>a</b>) new cell; (<b>b</b>) abused cell.</p>
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<p>SEM at 5k× with Secondary and Backscattering Electrons (SE/BSE) of the cathode: (<b>a</b>) new cell; (<b>b</b>) abused cell.</p>
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<p>Positive Temperature Coefficient (PTC) analysis. (<b>a</b>) PTC device; (<b>b</b>) brass cylinder with PTC inserted.</p>
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<p>PTC analysis. Test circuit scheme.</p>
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<p>PTC analysis. Resistance vs. temperature of brass cylinder with PTC and brass cylinder alone: (<b>a</b>) increasing branch at 1 A and following decreasing branch at 1 A; (<b>b</b>) increasing branch at 5 A.</p>
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<p>PTC analysis. Resistance and temperature of brass cylinder with PTC: (<b>a</b>) test performed at 1 A; (<b>b</b>) test performed at 5 A.</p>
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<p>PTC analysis. Resistance and temperature of brass cylinder with PTC after PTC triggering with 1 A: (<b>a</b>) heating—increasing temperature; (<b>b</b>) cooling—decreasing temperature.</p>
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14 pages, 6170 KiB  
Article
Vortex Domain Wall Thermal Pinning and Depinning in a Constricted Magnetic Nanowire for Storage Memory Nanodevices
by Mohammed Al Bahri, Salim Al-Kamiyani and Al Maha Al Habsi
Nanomaterials 2024, 14(18), 1518; https://doi.org/10.3390/nano14181518 - 19 Sep 2024
Viewed by 600
Abstract
In this study, we investigate the thermal pinning and depinning behaviors of vortex domain walls (VDWs) in constricted magnetic nanowires, with a focus on potential applications in storage memory nanodevices. Using micromagnetic simulations and spin transfer torque, we examine the impacts of device [...] Read more.
In this study, we investigate the thermal pinning and depinning behaviors of vortex domain walls (VDWs) in constricted magnetic nanowires, with a focus on potential applications in storage memory nanodevices. Using micromagnetic simulations and spin transfer torque, we examine the impacts of device temperature on VDW transformation into a transverse domain wall (TDW), mobility, and thermal strength pinning at the constricted area. We explore how thermal fluctuations influence the stability and mobility of domain walls within stepped nanowires. The thermal structural stability of VDWs and their pinning were investigated considering the effects of the stepped area depth (d) and its length (λ). Our findings indicate that the thermal stability of VDWs in magnetic stepped nanowires increases with decreasing the depth of the stepped area (d) and increasing nanowire thickness (th). For th ≥ 50 nm, the stability is maintained at temperatures ≥ 1200 K. In the stepped area, VDW thermal pinning strength increases with increasing d and decreasing λ. For values of d ≥ 100 nm, VDWs depin from the stepped area at temperatures ≥ 1000 K. Our results reveal that thermal effects significantly influence the pinning strength at constricted sites, impacting the overall performance and reliability of magnetic memory devices. These insights are crucial for optimizing the design and functionality of next-generation nanodevices. The stepped design offers numerous advantages, including simple fabrication using a single electron beam lithography exposure step on the resist. Additionally, adjusting λ and d allows for precise control over the pinning strength by modifying the dimensions of the stepped areas. Full article
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<p>The stepped nanowire dimensions of 1000 nm in length and 200 nm in width with a VDW.</p>
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<p>VDW dynamics show high structural stability in the stepped nanowire with pinning area dimensions of (<b>a</b>) (50 × 0 nm<sup>2</sup>), (<b>b</b>) (100 × 0 nm<sup>2</sup>), and (<b>c</b>) (150 × 0 nm<sup>2</sup>). (<b>d</b>) VDW transformation in the nanowire with stepped area dimensions of (200 × 0 nm<sup>2</sup>).</p>
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<p>VDW dynamics with high structural stability in the stepped nanowire with pinning area dimensions of (<b>a</b>) (50 × 50 nm<sup>2</sup>), (<b>b</b>) (100 × 50 nm<sup>2</sup>), and (<b>c</b>) (150 × 50 nm<sup>2</sup>). (<b>d</b>) VDW transformation in the nanowire with stepped area dimensions of (200 × 50 nm<sup>2</sup>).</p>
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<p>(<b>a</b>) VDW dynamics show high structural stability in the stepped nanowire with pinning area dimensions of (50 × 0 nm<sup>2</sup>). (<b>b</b>) The VDW reached the stepped area with high structural stability at a device temperature of 800 K. (<b>c</b>) The VDW transformation into TDW at a temperature of 1000 K. (<b>d</b>) <span class="html-italic">m<sub>x</sub></span> versus time for two curves with two temperature (<span class="html-italic">T</span>) values.</p>
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<p>(<b>a</b>) <span class="html-italic">T<sub>t</sub></span> as a function of <span class="html-italic">d</span> for two current density values. (<b>b</b>) <span class="html-italic">m<sub>x</sub></span> versus time for three curves with different <span class="html-italic">d</span> values and at <span class="html-italic">T<sub>t</sub></span>.</p>
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<p>(<b>a</b>) VDW transformation with a device thickness of 30 nm and (<b>b</b>) 40 nm. (<b>c</b>) VDW with higher structural stability with a device thickness of 50 nm. (<b>d</b>) <span class="html-italic">m<sub>x</sub></span> as a function of time for three different device thickness values and the device temperature of 600 K.</p>
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<p><span class="html-italic">T<sub>t</sub></span> as a function of device thickness for nanowires with stepped areas of 50 × 0 nm<sup>2</sup>, 100 × 0 nm<sup>2</sup>, and 150 × 0 nm<sup>2</sup>.</p>
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<p>VDW velocity as a function of the current density for nanowires under device temperatures of 300 K and 600 K in the stepped nanowire with dimensions of (<b>a</b>) 50 × 50 nm<sup>2</sup> and (<b>b</b>) 100 × 50 nm<sup>2</sup>.</p>
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<p>(<b>a</b>) VDW dynamics in a stepped nanowire with stepped dimensions of 50 × 50 nm<sup>2</sup>. (<b>b</b>) VDW pinning in the stepped area at a device temperature of 50 K. (<b>c</b>) VDW depinning from the stepped area at the device temperature of 150 K. (<b>d</b>) VDW depinning at a device temperature of 600 K with two vortices. (<b>e</b>) Magnetization components point along the <span class="html-italic">x</span>-direction (<span class="html-italic">m<sub>x</sub></span>) as a function of time at different device temperatures.</p>
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<p>(<b>a</b>) VDW dynamics in a stepped nanowire with stepped dimensions of 100 × 50 nm<sup>2</sup>. (<b>b</b>) VDW pinning in the stepped area at a device temperature of 600 K. (<b>c</b>) VDW depinning from the stepped area at a device temperature of 700 K. (<b>d</b>) Magnetization components pointing along the <span class="html-italic">x</span>-direction (<span class="html-italic">m<sub>x</sub></span>) as a function of time at different device temperatures (600 K, 700 K, and 1000 K).</p>
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<p>(<b>a</b>) VDW dynamics in a stepped nanowire with stepped dimensions of 150 × 50 nm<sup>2</sup>. (<b>b</b>) VDW pinning in the stepped area at a device temperature of 800 K. (<b>c</b>) VDW depinning from the stepped area at a device temperature of 950 K. (<b>d</b>) VDW dynamics in stepped nanowire with stepped dimensions of 200 × 50 nm<sup>2</sup>. (<b>e</b>) VDW pinning in the stepped area at a device temperature of 1000 K. (<b>f</b>) VDW depinning in the stepped area at the device temperature of 1400 K. (<b>g</b>) Magnetization components along the x-direction (<span class="html-italic">m<sub>x</sub></span>) over time at temperatures of 800 K, 1000 K, and 1200 K in a stepped nanowire of 150 × 50 nm<sup>2</sup>. (<b>h</b>) Magnetization components along the <span class="html-italic">x</span>-direction (<span class="html-italic">m<sub>x</sub></span>) over time at temperatures of 1000 K, 1400 K, and 1800 K in a stepped nanowire of 200 × 50 nm<sup>2</sup>.</p>
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<p>(<b>a</b>) VDW dynamics in stepped nanowire with stepped dimensions of 100 × 100 nm<sup>2</sup>. (<b>b</b>) VDW pinning in the stepped area (100 × 100 nm<sup>2</sup>) at a device temperature of 400 K. (<b>c</b>) VDW depinning from the stepped area (100 × 100 nm<sup>2</sup>) at the device temperature of 600 K. (<b>d</b>) The analysis of the magnetization components along the x-direction (<span class="html-italic">m<sub>x</sub></span>) over time at temperatures of 400 K, 600 K, and 800 K in a stepped nanowire of 100 × 100 nm<sup>2</sup>. (<b>e</b>) Magnetization components along the <span class="html-italic">x</span>-direction (<span class="html-italic">m<sub>x</sub></span>) over time at temperatures of 200 K, 400 K, and 600 K in a stepped nanowire of 100 × 150 nm<sup>2</sup>. (<b>f</b>) Magnetization components along the <span class="html-italic">x</span>-direction (<span class="html-italic">m<sub>x</sub></span>) over time at temperatures of 50 K, 200 K, and 400 K in a stepped nanowire of 100 × 200 nm<sup>2</sup>.</p>
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<p>(<b>a</b>) The plot of <span class="html-italic">T<sub>d</sub></span> as a function of <span class="html-italic">d</span> for two values of current density and λ = 50 nm. (<b>b</b>) The plot of <span class="html-italic">T<sub>d</sub></span> versus <span class="html-italic">λ</span> and <span class="html-italic">d</span> = 100 nm.</p>
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<p>The stepped area diagonal (D) with dimensions of <span class="html-italic">λ</span> and <math display="inline"><semantics> <mrow> <mi>p</mi> </mrow> </semantics></math>, where <math display="inline"><semantics> <mrow> <msup> <mrow> <mi>D</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msup> <mo>=</mo> <msup> <mrow> <mi>λ</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msup> <mo>+</mo> <msup> <mrow> <mi>p</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msup> </mrow> </semantics></math>.</p>
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<p>(<b>a</b>) VDW energy as a function of time for three device temperatures with a stepped area of 50 × 50 nm<sup>2</sup>. (<b>b</b>) VDW energy versus time for three values of device temperatures with a stepped area of 100 × 50 nm<sup>2</sup>.</p>
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22 pages, 7848 KiB  
Article
Improving Vehicle Warm-Up Performance Using Phase-Change Materials and Thermal Storage Methods
by Juho Lee, Jungkoo Lee and Kihyung Lee
Energies 2024, 17(18), 4556; https://doi.org/10.3390/en17184556 - 11 Sep 2024
Viewed by 626
Abstract
This study investigates the enhancement of vehicle warm-up performance using phase-change materials (PCMs) and various thermal storage methods. The primary objective is to utilize the thermal energy lost during engine cooling to improve the cold-start performance, thereby reducing fuel consumption and emissions. Thermal [...] Read more.
This study investigates the enhancement of vehicle warm-up performance using phase-change materials (PCMs) and various thermal storage methods. The primary objective is to utilize the thermal energy lost during engine cooling to improve the cold-start performance, thereby reducing fuel consumption and emissions. Thermal storage devices incorporating PCMs were developed and tested by measuring temperature changes and energy transfer over soaking periods of 4, 8, 16, and 24 h. The results show energy transfers of 591, 489, 446, and 315 kJ at 4, 8, 16, and 24 h, respectively. In terms of the warm-up time, the use of thermal storage devices reduced the time required to reach 70 °C by up to 24.45%, with significant reductions observed across all soaking periods. This reduction in the warm-up time directly contributes to faster engine stabilization, leading to proportional improvements in fuel efficiency and a corresponding decrease in exhaust emissions, including CO2. The findings highlight the effectiveness of PCMs in improving the engine warm-up performance and emphasize the importance of optimizing thermal storage systems to balance energy efficiency and practical application considerations. Additionally, the experimental data provide useful benchmark information for computational simulation validation, enabling the further optimization of automotive thermal management systems. Integrating a PCM-based thermal storage device can significantly enhance a vehicle’s warm-up performance, leading to reduced fuel consumption and lower emissions. Full article
(This article belongs to the Section D: Energy Storage and Application)
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<p>Diagram of the thermal storage device with a heat exchanger.</p>
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<p>Diagram of the thermal storage device with a tub.</p>
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<p>Schematic diagram of the heat storage system installed in the engine test rig.</p>
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<p>Setup of bench test.</p>
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<p>Thermal storage device with a vacuum chamber.</p>
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<p>Temperature changes during soaking over time.</p>
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<p>Test results for engines without thermal storage devices by case.</p>
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<p>Test results for engines with thermal storage device A-1.</p>
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<p>Test results for engines with thermal storage device A-2.</p>
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<p>Test results for engines with thermal storage device B-1.</p>
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<p>Test results for engines with thermal storage device B-2.</p>
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<p>Test results for 4 h of soaking as compared by the thermal storage device.</p>
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<p>Test results for 8 h of soaking as compared by the thermal storage device.</p>
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<p>Test results for 16 h of soaking as compared by the thermal storage device.</p>
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<p>Test results for 24 h of soaking as compared by the thermal storage device.</p>
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<p>Comparison of warm-up times by case.</p>
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<p>Comparison of transferred energy by case.</p>
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<p>Comparison of accumulated transferred energy values by case.</p>
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<p>Comparison of transferred energy by soaking time.</p>
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<p>Comparison of transferred energy by thermal storage device.</p>
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13 pages, 2633 KiB  
Article
Pyrrolidinium-Based Ionic Liquids as Advanced Non-Aqueous Electrolytes for Safer Next Generation Lithium Batteries
by Antía Santiago-Alonso, José Manuel Sánchez-Pico, Raquel San Emeterio, María Villanueva, Josefa Salgado and Juan José Parajó
Batteries 2024, 10(9), 319; https://doi.org/10.3390/batteries10090319 - 10 Sep 2024
Viewed by 696
Abstract
In the current context of increasing energy demand, ionic liquids (ILs) are presented as possible candidates to replace conventional electrolytes and to develop more efficient energy storage devices. The IL 1-Methyl-1-propylpyrrolidinium bis(trifluoromethanesulfonyl)imide has been selected for this work, due to the good thermal [...] Read more.
In the current context of increasing energy demand, ionic liquids (ILs) are presented as possible candidates to replace conventional electrolytes and to develop more efficient energy storage devices. The IL 1-Methyl-1-propylpyrrolidinium bis(trifluoromethanesulfonyl)imide has been selected for this work, due to the good thermal and chemical stabilities and good electrochemical performance of the pyrrolidinium cation based ILs. Binary mixtures of this IL and lithium salt with the same anion, [TFSI], have been prepared with the aim of assessing them, as possible electrolytes for lithium batteries. These mixtures were thermally and electrochemically characterised through DSC and dielectric spectroscopy studies. The ionic conductivity decreases as the salt concentration increases, finding values ranging between 0.4 S/m and 0.1 S/m at room temperature. Additionally, a wide liquid range was found for the mixtures, which would reduce or even eliminate some of the most common problems of current electrolytes, such as their crystallisation at low temperatures and flammability. Finally, the toxicity of pure IL and the intermediate salt concentration was also evaluated in terms of the bioluminescence inhibition of the Alivibrio Fischeri bacteria, observing that, although the toxicity increases with the salt addition, both samples can be classified as practically harmless. Full article
(This article belongs to the Special Issue Advances in Lithium-Ion Battery Safety and Fire)
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<p>DSC curves of binary mixtures [C<sub>3</sub>C<sub>1</sub>Pyrr][TFSI] with [Li][TFSI] at different concentrations (endo up).</p>
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<p>First (blue) and second (red) heating curves corresponding to 10 °C min<sup>−1</sup> and 5 °C min<sup>−1</sup> scan rates, respectively, for the pure and mixtures of IL + salt samples (endo up).</p>
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<p>DSC cooling-heating cycles at 10 °C min<sup>−1</sup> and 5 °C min<sup>−1</sup> of the mixture IL + [Li][TFSI] 0.2 m (endo up).</p>
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<p>(<b>a</b>) Ionic conductivity of binary mixtures [C<sub>3</sub>C<sub>1</sub>Pyrr][TFSI] and [Li][TFSI] against the [Li][TFSI] molar fraction at different temperatures. (<b>b</b>) Arrhenius plot showing the ionic conductivity vs. temperature for mixtures with different [Li][TFSI] content and their fitting to the Arrhenius equation.</p>
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<p>(<b>a</b>) Arrhenius plot of the ionic conductivity vs. temperature for mixtures with different [Li][TFSI] contents and their fitting to the VFT equation, and (<b>b</b>) activation energy and log (sigma) dependence on the molal concentration of lithium salt.</p>
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<p>Inhibition of bioluminescence for 30 min of exposure against the logarithm of the concentration of (<span style="color:#04B404">●</span>) [C<sub>3</sub>C<sub>1</sub>Pyrr][TFSI] and (<span style="color:#045FB4">●</span>) [C<sub>3</sub>C<sub>1</sub>Pyrr][TFSI] + [Li][TFSI] 0.5 m.</p>
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22 pages, 7586 KiB  
Article
Bi-Level Optimal Configuration of Electric Thermal Storage Boilers in Thermal–Electrical Integrated Energy System
by Xiaoming Zhang, Jiaoyang Feng, Guangzhe Liang, Chonglei Ding, Peihong Yang and Xin Zhang
Electronics 2024, 13(17), 3567; https://doi.org/10.3390/electronics13173567 - 8 Sep 2024
Viewed by 590
Abstract
Electric thermal storage boilers (ETSBs) are important devices in enhancing the electric–thermal decoupling ability and spatiotemporal transfer of integrated energy system (IES), which is beneficial for improving system flexibility and energy utilization efficiency. In order to obtain more accurate and comprehensive results, a [...] Read more.
Electric thermal storage boilers (ETSBs) are important devices in enhancing the electric–thermal decoupling ability and spatiotemporal transfer of integrated energy system (IES), which is beneficial for improving system flexibility and energy utilization efficiency. In order to obtain more accurate and comprehensive results, a bi-level optimal model is proposed to study the site selection and capacity configuration of ETSB in IES based on the established mathematical model of ETSB. The objective of upper-level optimization of the model is obtaining the lowest energy supply cost when configuring the location and capacity of ETSB, while the lower-level model optimizes the operation scheduling with the goal of obtaining the lowest operational cost. The mixed-integer linear programming method and the genetic algorithm method are selected to obtain the optimal model. To illustrate the effectiveness and advantages of the proposed method, case studies are carried out. The optimal configuration scheme for an ETSB is obtained by comparing the lowest energy supply cost under different configuration parameters. Furthermore, the impact of an ETSB on the system is also analyzed based on the variations in energy balance, abandoned energy, and energy allocation before and after configuring the ETSB. Full article
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<p>Framework diagram of an EH-IES.</p>
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<p>Energy flow diagram of ETSB.</p>
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<p>The expansion planning scheme of ETSB.</p>
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<p>Flowchart for the GA calculation of the lower level.</p>
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<p>Topology of the original EH-IES.</p>
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<p>The operational feasible region of the extraction condensing CHP unit.</p>
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<p>Electrical and thermal load demand curve. (<b>a</b>) Non-heating period; (<b>b</b>) heating period.</p>
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<p>Typical daily WP−PV output curve. (<b>a</b>) Non−heating period; (<b>b</b>) heating period.</p>
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<p>The relationship of optimal results and ETSB parameters. (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>0.5</mn> </mrow> </semantics></math>; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>1.0</mn> </mrow> </semantics></math>; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>1.5</mn> </mrow> </semantics></math>; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>2.0</mn> </mrow> </semantics></math>; (<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics></math>; (<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>3.0</mn> </mrow> </semantics></math>.</p>
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<p>The relationship of optimal results and ETSB parameters. (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>0.5</mn> </mrow> </semantics></math>; (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>1.0</mn> </mrow> </semantics></math>; (<b>c</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>1.5</mn> </mrow> </semantics></math>; (<b>d</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>2.0</mn> </mrow> </semantics></math>; (<b>e</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>2.5</mn> </mrow> </semantics></math>; (<b>f</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Q</mi> <mrow> <mi>o</mi> <mi>u</mi> <mi>t</mi> <mo>,</mo> <mi>max</mi> </mrow> </msub> <mo>=</mo> <mn>3.0</mn> </mrow> </semantics></math>.</p>
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<p>Power balance of the two schemes. (<b>a</b>) Non−heating period of the original scheme; (<b>b</b>) Heating period of the original scheme; (<b>c</b>) Non−heating period of the optimal scheme; (<b>d</b>) Heating period of the optimal scheme.</p>
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<p>Thermal balance of the two schemes. (<b>a</b>) Non−heating period of the original scheme; (<b>b</b>) Heating period of the original scheme; (<b>c</b>) Non−heating period of the optimal scheme; (<b>d</b>) Heating period of the optimal scheme.</p>
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<p>Thermal balance of the two schemes. (<b>a</b>) Non−heating period of the original scheme; (<b>b</b>) Heating period of the original scheme; (<b>c</b>) Non−heating period of the optimal scheme; (<b>d</b>) Heating period of the optimal scheme.</p>
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<p>The abandoned electricity in both schemes. (<b>a</b>) Non−heating period of the original scheme; (<b>b</b>) Heating period of the original scheme.</p>
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<p>Thermal storage state of the ETSB in the optimal scheme.</p>
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<p>The energy flow allocation of the system. (<b>a</b>) Original scheme; (<b>b</b>) Optimal scheme.</p>
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30 pages, 6045 KiB  
Article
Hybrid Control Strategy for 5G Base Station Virtual Battery-Assisted Power Grid Peak Shaving
by Siqiao Zhu, Rui Ma, Yang Zhou and Shiyuan Zhong
Electronics 2024, 13(17), 3488; https://doi.org/10.3390/electronics13173488 - 2 Sep 2024
Viewed by 828
Abstract
With the rapid development of the digital new infrastructure industry, the energy demand for communication base stations in smart grid systems is escalating daily. The country is vigorously promoting the communication energy storage industry. However, the energy storage capacity of base stations is [...] Read more.
With the rapid development of the digital new infrastructure industry, the energy demand for communication base stations in smart grid systems is escalating daily. The country is vigorously promoting the communication energy storage industry. However, the energy storage capacity of base stations is limited and widely distributed, making it difficult to effectively participate in power grid auxiliary services by only implementing the centralized control of base stations. Aiming at this issue, an interactive hybrid control mode between energy storage and the power system under the base station sleep control strategy is delved into in this paper. Grounded in the spatiotemporal traits of chemical energy storage and thermal energy storage, a virtual battery model for base stations is established and the scheduling potential of battery clusters in multiple scenarios is explored. Then, based on the time of use electricity price and user fitness indicators, with the maximum transmission signal and minimum operating cost as objective functions, a decentralized control device is used to locally and quickly regulate the communication system. Furthermore, a multi-objective joint peak shaving model for base stations is established, centrally controlling the energy storage system of the base station through a virtual battery management system. Finally, a simulation analysis was conducted on data from different types of base stations in the region, designing two distinct scheduling schemes for four regional categories. The analysis results demonstrate that the proposed model can effectively reduce the power consumption of base stations while mitigating the fluctuation of the power grid load. Full article
(This article belongs to the Section Power Electronics)
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<p>Distribution map of communication base stations within the region.</p>
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<p>The main composition diagram of the communication system.</p>
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<p>Temperature control principle diagram of temperature control system.</p>
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<p>Number of web users in different scenarios for 24 h.</p>
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<p>Sub-control area delineation of spatial extent.</p>
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<p>Virtual battery transaction flow.</p>
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<p>Virtual Battery Cluster Control Model Diagram.</p>
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<p>Flow Chart for Optimizing Base Station Battery Scheduling Based on ADMM.</p>
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<p>Daily load profile and number of user connections in a typical area of a base station.</p>
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<p>Diagram of the minimum battery backup status of 1000 base station batteries for four types of typical scenarios.</p>
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<p>Minimum backup state diagram of base station batteries after reduction for four typical scenarios.</p>
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<p>Minimum backup state diagram of base station batteries after reduction for four typical scenarios.</p>
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<p>Graph of the minimum state of power reserve for the four types of scenarios in the virtual battery management system.</p>
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<p>Variation curve of outdoor temperature in 24 h area.</p>
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<p>Plot of adjustable temperature intervals for base station temperature after aggregation for four types of typical regions.</p>
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<p>Four types of regional network fee incentive factor settings.</p>
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<p>Comparison of base station operation before and after office area optimization.</p>
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<p>Power consumption and number of operations before and after base station sleep for four types of base stations.</p>
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<p>Power consumption and number of operations before and after base station sleep for four types of base stations.</p>
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<p>Comparison of base station hybrid control participation in grid peaking.</p>
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14 pages, 3070 KiB  
Article
One-Step Synthesis of Heterostructured Mo@MoO2 Nanosheets for High-Performance Supercapacitors with Long Cycling Life and High Rate Capability
by Ao Cheng, Yan Shen, Tao Cui, Zhe Liu, Yu Lin, Runze Zhan, Shuai Tang, Yu Zhang, Huanjun Chen and Shaozhi Deng
Nanomaterials 2024, 14(17), 1404; https://doi.org/10.3390/nano14171404 - 28 Aug 2024
Viewed by 991
Abstract
Supercapacitors have gained increased attention in recent years due to their significant role in energy storage devices; their impact largely depends on the electrode material. The diversity of energy storage mechanisms means that various electrode materials can provide unique benefits for specific applications, [...] Read more.
Supercapacitors have gained increased attention in recent years due to their significant role in energy storage devices; their impact largely depends on the electrode material. The diversity of energy storage mechanisms means that various electrode materials can provide unique benefits for specific applications, highlighting the growing trend towards nanocomposite electrodes. Typically, these nanocomposite electrodes combine pseudocapacitive materials with carbon-based materials to form heterogeneous structural composites, often requiring complex multi-step preparation processes. This study introduces a straightforward approach to fabricate a non-carbon-based Mo@MoO2 nanosheet composite electrode using a one-step thermal evaporating vapor deposition (TEVD) method. This novel electrode features Mo at the core and MoO2 as the shell and demonstrates exceptional electrochemical performance. Specifically, at a current density of 1 A g−1, it achieves a storage capacity of 205.1 F g−1, maintaining virtually unchanged capacity after 10,000 charge–discharge cycles at 2 A g−1. The outstanding long-cycle stability is ascribed to the vertical two-dimensional geometry, the superior conductivity, and pseudocapacitance of the Mo@MoO2 core-shell nanosheets. These attributes significantly improve the electrode’s charge storage capacity, charge transfer speed, and structural integrity during the cycling process. The development of the one-step grown Mo@MoO2 nanosheets offers a promising way for the advancement of high-performance, non-carbon-based supercapacitor nanocomposite electrodes. Full article
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<p>(<b>a</b>) Typical SEM images of the Ni foam framework substrate before and after the TEVD synthesis of Mo@MoO<sub>2</sub> core-shell heterostructured nanosheets, and the corresponding schematic diagrams. (<b>b</b>) Depiction of ion/electron transport behavior during the charge–discharge process.</p>
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<p>Micro-morphologies and structure of the Mo@MoO<sub>2</sub> nanosheets. (<b>a</b>,<b>b</b>) SEM images at different magnifications. (<b>c</b>) Low-magnification TEM image. (<b>d</b>) HRTEM image of the marked area D in (<b>c</b>). (<b>e</b>) The SEAD pattern of the nanosheet in (<b>c</b>). (<b>f</b>) The Inverse Fourier Transform result of the marked area F in (<b>d</b>).</p>
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<p>XRD characterization of the prepared Mo@MoO<sub>2</sub> nanosheets (compared with Mo, MoO<sub>2</sub> and Ni standard PDF phase cards, respectively).</p>
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<p>XPS analysis of the prepared Mo@MoO<sub>2</sub> nanosheets. (<b>a</b>) Wide-scanning survey XPS spectrum. (<b>b</b>–<b>d</b>) High-resolution XPS spectra of C 1s, O 1s, and Mo 3d in Mo@MoO<sub>2</sub>, respectively.</p>
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<p>Thermogravimetric analysis of pure Mo powder and prepared Mo@MoO<sub>2</sub> nanosheets. (<b>a</b>) Derivative thermogravimetric (DTG) curves. (<b>b</b>) Thermogravimetric analyzer (TGA) curves.</p>
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<p>Electrochemical performance of the Mo@MoO<sub>2</sub> nanosheets electrode. (<b>a</b>) Nyquist plots. Insets: the enlarged high-frequency and medium-high-frequency regions of Nyquist plots and the equivalent circuit model. (<b>b</b>) CV curves at different scanning rates from 10 to 100 mV s<sup>−1</sup>. (<b>c</b>) GCD curves at different current densities from 1 to 10 A g<sup>−1</sup>. (<b>d</b>) Rate capability curve with increasing current density. (<b>e</b>) Long cycling performance at a current density of 2.0 A g<sup>−1</sup>. Insets: the enlarged charge–discharge curves of the first three and the last three cycles, and an image showing the function of a green LED light powered by the assembled coin-type symmetrical supercapacitor.</p>
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