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Search Results (1,984)

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Keywords = charge estimations

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23 pages, 3716 KiB  
Article
Evaluation of Battery Management Systems for Electric Vehicles Using Traditional and Modern Estimation Methods
by Muhammad Talha Mumtaz Noreen, Mohammad Hossein Fouladfar and Nagham Saeed
Network 2024, 4(4), 586-608; https://doi.org/10.3390/network4040029 (registering DOI) - 21 Dec 2024
Viewed by 224
Abstract
This paper presents the development of an advanced battery management system (BMS) for electric vehicles (EVs), designed to enhance battery performance, safety, and longevity. Central to the BMS is its precise monitoring of critical parameters, including voltage, current, and temperature, enabled by dedicated [...] Read more.
This paper presents the development of an advanced battery management system (BMS) for electric vehicles (EVs), designed to enhance battery performance, safety, and longevity. Central to the BMS is its precise monitoring of critical parameters, including voltage, current, and temperature, enabled by dedicated sensors. These sensors facilitate accurate calculations of the state of charge (SOC) and state of health (SOH), with real-time data displayed through an IoT cloud interface. The proposed BMS employs data-driven approaches, like advanced Kalman filters (KF), for battery state estimation, allowing continuous updates to the battery state with improved accuracy and adaptability during each charging cycle. Simulation tests conducted in MATLAB’s Simulink across multiple charging and discharging cycles demonstrate the superior accuracy of the advanced Kalman filter (KF), in handling non-linear battery behaviours. Results indicate that the proposed BMS achieves a significantly lower error margin in SOC tracking, ranging from 0.32% to 1%, compared to traditional methods with error margins up to 5%. These findings underscore the importance of integrating robust sensor systems in BMSs to optimise EV battery management, reduce maintenance costs, and improve battery sustainability. Full article
11 pages, 257 KiB  
Article
Respiratory Diseases with High Occupational Fraction in Italy: Results from the Italian Hospital Discharge Registry (2010–2021)
by Pierpaolo Ferrante
Healthcare 2024, 12(24), 2565; https://doi.org/10.3390/healthcare12242565 - 20 Dec 2024
Viewed by 249
Abstract
Objectives: Occupational respiratory diseases represent a major public health concern worldwide. This study analyses the hospitalization costs and characteristics of four major occupational respiratory diseases: malignant mesothelioma (MM), sinonasal cancer (SNC), pneumoconiosis (PN), and hypersensitivity pneumonitis (HP). The findings are situated within the [...] Read more.
Objectives: Occupational respiratory diseases represent a major public health concern worldwide. This study analyses the hospitalization costs and characteristics of four major occupational respiratory diseases: malignant mesothelioma (MM), sinonasal cancer (SNC), pneumoconiosis (PN), and hypersensitivity pneumonitis (HP). The findings are situated within the context of Italy’s population trends and healthcare system, offering insights into the economic and clinical burden of these diseases. Study Design: This retrospective, population-based study examines Italian hospitalizations for MM, SNC, PN, and HP during the period 2010–2021. The primary outcomes were the number of hospitalizations, length of stay, and associated cost. Costs were derived from charges linked to diagnosis-related groups (version 24) and major diagnostic category coding systems. Results: Though the Italian population is rapidly aging, the annual number and rate of hospitalizations declined by 35% over the study period. SNC hospitalizations aligned with the overall trend, PN and MM experienced faster declines, whereas HP admissions remained steady. MM emerged as the most resource-intensive (EUR 25 million yearly, with 86% attributable to occupation), followed by PN (EUR 10 million, entirely occupational), SNC (EUR 5 million, with EUR 650,000 occupational), and HP (EUR 2 million, with EUR 370,000 occupational). All studied diseases had an average length of stay exceeding the national one. The SNC admissions were the shortest (6.5 days) and least expensive (EUR 3647). In contrast, MM, PN, and HP had a mean length of stay exceeding 10 days, with admission costs averaging EUR 4700 for MM and EUR 4000 for PN and HP. The median age was the highest for PN (78 years) and MM (71 years), while SNC and HP patients had a median age of approximately 65 years. Conclusions: Consistent with their anticipated benefits, Italian workplace health regulations over the last three decades, including the 1992 asbestos ban and D.lgs. 81/2008, are associated with significant reductions in the hospitalization burden and an increased median age at discharge for MM and PN. In contrast, fewer conclusions can be drawn for SNC and HP due to their lower occupational fractions (10–20%). This finding suggests adding an occupational exposure flag in hospital records for acknowledged occupational diseases to enhance surveillance. Finally, this study provides the first estimate of the occupational fraction of hospitalization costs for the studied diseases in Italy. Full article
(This article belongs to the Section Environmental Factors and Global Health)
24 pages, 3125 KiB  
Article
Lithium Battery SOC Estimation Based on Type-2 Fuzzy Cerebellar Model Neural Network
by Jing Zhao, Menglei Ge, Qiyu Huang and Xungao Zhong
Electronics 2024, 13(24), 4999; https://doi.org/10.3390/electronics13244999 - 19 Dec 2024
Viewed by 263
Abstract
Accurate estimation of the state of charge (SOC) of lithium batteries is critical for the safe and optimal operation of battery management systems (BMSs). Traditional SOC estimation methods are often limited by model inaccuracy and noise interference. In this study, a novel type-2 [...] Read more.
Accurate estimation of the state of charge (SOC) of lithium batteries is critical for the safe and optimal operation of battery management systems (BMSs). Traditional SOC estimation methods are often limited by model inaccuracy and noise interference. In this study, a novel type-2 fuzzy cerebellar model neural network (Type-2 FCMNN) is proposed for accurately estimating the state of charge of lithium batteries. Based on the traditional fuzzy cerebellar model neural network (FCMNN), type-2 fuzzy rules are innovatively introduced to enhance the robustness of the model against uncertainties and noise disturbances. This enables the model to better cope with nonlinear complexity and external disturbances when dealing with SOC estimation of lithium batteries and significantly improves the accuracy of prediction. On this basis, by analyzing the working principle of lithium batteries, a battery equivalent circuit model is successfully established and simulated and tested by Simulink R2022b, which provides a theoretical basis for the selection of the size of the input parameters of the subsequent neural network. Then, this paper designs and implements the SOC estimation model based on Type-2 FCMNN and tests it in Matlab. Finally, this paper carries out simulation comparison experiments between Type-2 FCMNN and various classical neural network algorithms in Matlab R2022b including traditional FCMNN, a backpropagation neural network, radial basis function neural network, and Kalman filtering algorithm. The simulation results show that Type-2 FCMNN exhibits a significant advantage in SOC estimation accuracy, with mean absolute error and root mean square error values of only 43.1% and 36.0% of FCMNN’s, respectively, while FCMNN achieves the best results among the compared methods. Full article
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<p>Schematic diagram of the internal electrochemical reaction of a lithium-ion battery.</p>
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<p>Schematic diagram of the voltage rebound phenomenon of a lithium battery.</p>
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<p>Model diagram of a second-order RC equivalent circuit.</p>
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<p>Lithium battery experimental equipment and data acquisition system.</p>
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<p>Experimental-voltage-current diagram for OCV working condition at 0 °C.</p>
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<p>Simulink simulation of the second-order RC circuit model.</p>
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<p>Schematic diagram of Gaussian type-2 fuzzy affiliation function.</p>
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<p>Architecture of the Type-2 FCMNN algorithm.</p>
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<p>Organisation of Type-2 FCMNN.</p>
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<p>Flow chart of the Type-2 FCMNN SOC estimation method.</p>
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<p>Plot of Type-2 FCMNN SOC forecast SOC under OCV conditions.</p>
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<p>Plot of BPNN SOC forecast results under OCV conditions.</p>
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<p>Plot of RBFNN SOC forecast results under OCV conditions.</p>
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<p>Plot of KF SOC forecast results under OCV conditions.</p>
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<p>Plot of FCMNN SOC forecast results under OCV conditions.</p>
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<p>Experimental-voltage-current diagram for DST-FUDS under working conditions at 0 °C.</p>
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<p>Experimental voltage–current diagram for DST-FUDS under working conditions at 0 °C.</p>
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<p>Plot of Type-2 FCMNN SOC forecast results under DST-FUDS conditions.</p>
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<p>Plot of BPNN SOC forecast results under DST-FUDS conditions.</p>
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<p>Plot of RBFNN SOC forecast results under DST-FUDS conditions.</p>
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<p>Plot of KF SOC forecast results under DST-FUDS conditions.</p>
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<p>Plot of FCMNN SOC forecast results under DST-FUDS conditions.</p>
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23 pages, 13973 KiB  
Article
Joint Fault Diagnosis of IGBT and Current Sensor in LLC Resonant Converter Module Based on Reduced Order Interval Sliding Mode Observer
by Xi Zha, Wei Feng, Xianfeng Zhang, Zhonghua Cao and Xinyang Chen
Sensors 2024, 24(24), 8077; https://doi.org/10.3390/s24248077 - 18 Dec 2024
Viewed by 259
Abstract
LLC resonant converters have emerged as essential components in DC charging station modules, thanks to their outstanding performance attributes such as high power density, efficiency, and compact size. The stability of these converters is crucial for vehicle endurance and passenger experience, making reliability [...] Read more.
LLC resonant converters have emerged as essential components in DC charging station modules, thanks to their outstanding performance attributes such as high power density, efficiency, and compact size. The stability of these converters is crucial for vehicle endurance and passenger experience, making reliability a top priority. However, malfunctions in the switching transistor or current sensor can hinder the converter’s ability to maintain a resonant state and stable output voltage, leading to a notable reduction in system efficiency and output capability. This article proposes a fault diagnosis strategy for LLC resonant converters utilizing a reduced-order interval sliding mode observer. Initially, an augmented generalized system for the LLC resonant converter is developed to convert current sensor faults into generalized state vectors. Next, the application of matrix transformations plays a critical role in decoupling open-circuit faults from the inverter system’s state and current sensor faults. To achieve accurate estimation of phase currents and detection of current sensor faults, a reduced-order interval sliding mode observer has been designed. Building upon the estimation results generated by this observer, a diagnostic algorithm featuring adaptive thresholds has been introduced. This innovative algorithm effectively differentiates between current sensor faults and open switch faults, enhancing fault detection accuracy. Furthermore, it is capable of localizing faulty power switches and estimating various types of current sensor faults, thereby providing valuable insights for maintenance and repair. The robustness and effectiveness of the proposed fault diagnosis algorithm have been validated through experimental results and comparisons with existing methods, confirming its practical applicability in real-world inverter systems. Full article
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<p>The topology of Charging Module.</p>
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<p>LLC resonant converter circuit topology diagram.</p>
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<p>Equivalent diagram of LLC resonant converter circuit.</p>
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<p>phase-k current flow path under normal working conditions.</p>
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<p>Phase-k current flow path in case of <math display="inline"><semantics> <msub> <mi>S</mi> <mrow> <mi>k</mi> <mn>1</mn> </mrow> </msub> </semantics></math> open circuit fault.</p>
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<p>Fault diagnosis process.</p>
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<p>Hardware in the loop experimental device.</p>
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<p>Diagnosis results of open circuit fault of power switch tube <math display="inline"><semantics> <msub> <mi>S</mi> <mrow> <mi>a</mi> <mn>2</mn> </mrow> </msub> </semantics></math>.</p>
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<p>Drift fault diagnosis results of DC side current sensor.</p>
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<p>Diagnosis results of DC side current sensor offset fault.</p>
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<p>Robustness verification results of <math display="inline"><semantics> <msub> <mi>S</mi> <mrow> <mi>b</mi> <mn>2</mn> </mrow> </msub> </semantics></math> open circuit fault under DC voltage fluctuation fluctuations.</p>
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<p>Verification results of gain fault robustness under sudden changes in DC side load parameters.</p>
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21 pages, 4946 KiB  
Article
Simple Energy Model for Hydrogen Fuel Cell Vehicles: Model Development and Testing
by Kyoungho Ahn and Hesham A. Rakha
Energies 2024, 17(24), 6360; https://doi.org/10.3390/en17246360 - 18 Dec 2024
Viewed by 299
Abstract
Hydrogen fuel cell vehicles (HFCVs) are a promising technology for reducing vehicle emissions and improving energy efficiency. Due to the ongoing evolution of this technology, there is limited comprehensive research and documentation regarding the energy modeling of HFCVs. To address this gap, the [...] Read more.
Hydrogen fuel cell vehicles (HFCVs) are a promising technology for reducing vehicle emissions and improving energy efficiency. Due to the ongoing evolution of this technology, there is limited comprehensive research and documentation regarding the energy modeling of HFCVs. To address this gap, the paper develops a simple HFCV energy consumption model using new fuel cell efficiency estimation methods. Our HFCV energy model leverages real-time vehicle speed, acceleration, and roadway grade data to determine instantaneous power exertion for the computation of hydrogen fuel consumption, battery energy usage, and overall energy consumption. The results suggest that the model’s forecasts align well with real-world data, demonstrating average error rates of 0.0% and −0.1% for fuel cell energy and total energy consumption across all four cycles. However, it is observed that the error rate for the UDDS drive cycle can be as high as 13.1%. Moreover, the study confirms the reliability of the proposed model through validation with independent data. The findings indicate that the model precisely predicts energy consumption, with an error rate of 6.7% for fuel cell estimation and 0.2% for total energy estimation compared to empirical data. Furthermore, the model is compared to FASTSim, which was developed by the National Renewable Energy Laboratory (NREL), and the difference between the two models is found to be around 2.5%. Additionally, instantaneous battery state of charge (SOC) predictions from the model closely match observed instantaneous SOC measurements, highlighting the model’s effectiveness in estimating real-time changes in the battery SOC. The study investigates the energy impact of various intersection controls to assess the applicability of the proposed energy model. The proposed HFCV energy model offers a practical, versatile alternative, leveraging simplicity without compromising accuracy. Its simplified structure reduces computational requirements, making it ideal for real-time applications, smartphone apps, in-vehicle systems, and transportation simulation tools, while maintaining accuracy and addressing limitations of more complex models. Full article
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<p>Driving cycles: (<b>a</b>) UDDS, (<b>b</b>) HWFET, (<b>c</b>) NEDC, and (<b>d</b>) speed.</p>
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<p>HFCV energy consumption and required vehicle power: (<b>a</b>) battery energy, (<b>b</b>) fuel cell, and (<b>c</b>) fuel cell and battery energy.</p>
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<p>Boundary condition for battery mode.</p>
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<p>Fuel cell driveline efficiency estimation.</p>
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<p>Model prediction of NEDC: (<b>a</b>) fuel cell consumption and (<b>b</b>) total consumption.</p>
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<p>Model validation of JC08: (<b>a</b>) fuel cell consumption and (<b>b</b>) total consumption.</p>
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<p>NEDC SOC estimation.</p>
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<p>Model comparison with FASTSim results: (<b>a</b>) UDDS, (<b>b</b>) HWFET, and (<b>c</b>) NEDC.</p>
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<p>Simulation test results. (<b>a</b>) HFCV, (<b>b</b>) ICEV, (<b>c</b>) BEV, and (<b>d</b>) HEV. (<b>e</b>) Average delay per vehicle.</p>
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24 pages, 19392 KiB  
Article
Platinum Compound on Gold–Magnesia Hybrid Structure: A Theoretical Investigation on Adsorption, Hydrolysis, and Interaction with DNA Purine Bases
by Zhenjun Song, Mingyue Liu, Aiguo Zhong, Meiding Yang, Zhicai He, Wenmin Wang and Hongdao Li
Nanomaterials 2024, 14(24), 2027; https://doi.org/10.3390/nano14242027 - 17 Dec 2024
Viewed by 301
Abstract
Cisplatin-based platinum compounds are important clinical chemotherapeutic agents that participate in most tumor chemotherapy regimens. Through density-functional theory calculations, the formation and stability of the inorganic oxide carrier, the mechanisms of the hydrolysis reaction of the activated platinum compound, and its binding mechanism [...] Read more.
Cisplatin-based platinum compounds are important clinical chemotherapeutic agents that participate in most tumor chemotherapy regimens. Through density-functional theory calculations, the formation and stability of the inorganic oxide carrier, the mechanisms of the hydrolysis reaction of the activated platinum compound, and its binding mechanism with DNA bases can be studied. The higher the oxidation state of Pt (II to IV), the more electrons transfer from the magnesia–gold composite material to the platinum compound. After adsorption on the composite carrier, 5d←2p coordination bonds of Pt-N are strengthened. For flat and oblique adsorption modes of cisplatin, there is no significant difference in the density of states of the gold and magnesium oxide film, indicating the maintenance of the heterojunction structural framework. However, there are significant changes in the electronic states of cisplatin itself with different adsorption configurations. In the flat configuration, the band gap width of cisplatin is larger than that of the oblique configuration. The Cl-Pt bond range in the Pt(III) compound shows a clear charge reduction on the magnesia film, indicating the Cl-Pt bond is an active site with the potential for decomposition and hydrolysis. The substitution of chloride ions by water can lead to hydrolysis products, enhancing the polarization of the composite and showing strong charge separation. The hydrolysis of the free platinum compound is endothermic by 0.309 eV, exceeding the small activation energy barrier of 0.399 eV, indicating that hydrolysis of this platinum compound is easily achievable. ADME (absorption, distribution, metabolism, and excretion) prediction parameters indicate that hydrolysis products have good ESOL (Estimated SOLubility) solubility and high gastrointestinal absorption, consistent with Lipinski’s rule. During the coordination reaction process, there are significant changes in the distribution of frontier molecular orbitals, with the HOMO (highest occupied molecular orbital) of the initial state primarily located on the purine base, providing the possibility for electron transfer to the empty orbitals of the platinum compound in the LUMO (lowest unoccupied molecular orbital). The HOMO and HOMO-1 of the transition state and product are mainly distributed on the platinum compound, indicating clear electron transfer and orbital rearrangement. The activation energy barrier for the purine coordination reaction with the hydrolysis products is reduced to 0.61 eV, and the dipole moment gradually decreases to 6.77 Debye during the reaction, indicating a reduction in the system’s charge separation and polarization. This contribution is anticipated to provide a new theoretical clue for developing inorganic oxide carriers of platinum compounds. Full article
(This article belongs to the Section Biology and Medicines)
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<p>The structure and charge population of gold (111) film fully optimized with gamma point and (2 × 2 × 1) k-point meshing. The Au-Au distances and charges in parentheses correspond to the values obtained at denser (2 × 2 × 1) k-point meshing.</p>
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<p>The structure and charge population of gold (111)-supported magnesia (111) film. (<b>a</b>,<b>b</b>) correspond to the stable equilibrium structure, while (<b>c</b>,<b>d</b>) correspond to the unstable structure with perpendicular gold-oxygen bonds. Green and red balls represent magnesium and oxygen atoms, and the pink, cyan, and brown balls represent top-layer, second-layer, and bottom-two-layer gold atoms.</p>
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<p>The differential charge density contour with charge density isosurface value of 0.001 e Bohr<sup>−3</sup> (<b>a</b>,<b>b</b>) and localized density of states for gold (111)-supported magnesia (111) film (<b>c</b>). The yellow and cyan slices represent electron accumulation and electron depletion areas, respectively.</p>
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<p>Adsorption and transformation of cisplatin compound on gold-supported 1 ML ultrathin magnesia (111). The Gibbs free energies are shown relative to the ground-state molecular adsorption state with flat adsorption configuration and Gibbs free energy of −380.373 eV. The white, blue, red, purple-, green-, cyan-, and yellow-colored balls stand for H, N, O, Cl, Mg, Pt, and Au, respectively.</p>
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<p>Charge density contours with isosurface value 0.05 e Bohr<sup>−3</sup> (<b>a</b>), highest occupied molecular orbital and lowest unoccupied molecular orbital of cisplatin molecule (<b>b</b>), and differential charge density contours (<b>c</b>) with isosurface value 0.001 e Bohr<sup>−3</sup>. For differential charge density, the isosurfaces colored in turquoise and dark yellow represent charge accumulation and depletion, respectively.</p>
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<p>Localized density of states of platinum central ion, coordinated ammonia nitrogen, chloride ions, magnesium, oxygen, and gold slab for flat adsorption configuration (<b>a</b>,<b>b</b>) and oblique adsorption configuration (<b>c</b>,<b>d</b>).</p>
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<p>Charge density contours with isosurface value 0.15 e Bohr<sup>−3</sup> (<b>a</b>) and differential charge density contours with isosurface value 0.003 e Bohr<sup>−3</sup> (<b>b</b>) for Pt(III) compound adsorption on gold-supported magnesia (111) film. The isosurfaces colored in dark yellow and turquoise represent charge accumulation and charge depletion, respectively.</p>
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<p>The hydrolysis of adsorbed cisplatin occurs gradually by water substitution. The assumed structure for water adsorption with oxygen linked with platinum (<b>a</b>), the optimized structure for water adsorption with hydrogen linked with platinum (<b>b</b>), water adsorption on ammonia (<b>c</b>), the water substitution structure (<b>d</b>), the water adsorption energy (<b>e</b>) and Bader charge for structural sites of water adsorption on platinum (<b>f</b>) and hydrolysis product (<b>g</b>).</p>
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<p>Potential energy diagram for hydrolysis reaction for Pt(III) compound on magnesia film. Structural models show relaxed structures for water adsorption on ammonia ligand (initial state), transition state, and water substitution product. The star * represents adsorption site.</p>
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<p>Potential energy diagram for the hydrolysis reaction in the first step for a free Pt(III) compound. Structural models show relaxed structures for water adsorption on ammonia ligands (initial state), transition state (TS), and water-substituted product.</p>
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<p>Potential energy diagram for second step hydrolysis reaction for free Pt(III) compound. Structural models show relaxed structures for water adsorption on ammonia ligand (initial state), transition state (TS), and water-substituted product.</p>
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<p>Potential energy diagram for guanine interaction with the Pt(III) compound. Relaxed structures for physical adduct with hydrogen bonding (initial state), transition state (TS), and the formation of coordination bond (final state).</p>
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<p>The optimized structures with dipole moment vectors (shown in red arrows), LUMO and HOMO frontier orbitals for reactant (IS), transition state (TS), and final product (FS, (<b>a</b>)); the electron spin density for reactant (<b>b</b>) and final product (<b>c</b>); the platinum NBO charge population (<b>d</b>), enthalpy diagram (<b>e</b>), N(Guanine)-Pt distance (<b>f</b>) and dipole moment analysis (<b>g</b>). The isosurface values for molecular orbital and electronic density are 0.02 and 0.0004, respectively.</p>
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<p>Temperature influence on the energetics (<span class="html-italic">U, H, G</span>) of primary platinum hydrolysis species (<b>a</b>), the initial reactant adduct (<b>b</b>), the coordination product (<b>c</b>), and the coordination reaction energy of primary platinum hydrolysis species interacting with guanine (<b>d</b>).</p>
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<p>The energetics, dipole moment, Cl-Pt distance, Wiberg bond index, and N(5′-guanylic acid) Mulliken charge during coordination reaction between 5′-guanylic acid and platinum compound.</p>
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18 pages, 3568 KiB  
Article
Hydrogen Diffusion in Deformed Austenitic TRIP Steel—A Study of Mathematical Prediction and Experimental Validation
by Christian Hempel, Marcel Mandel, Caroline Quitzke, Marco Wendler, Thilo Kreschel, Olena Volkova and Lutz Krüger
Materials 2024, 17(24), 6114; https://doi.org/10.3390/ma17246114 - 13 Dec 2024
Viewed by 488
Abstract
This study focuses on the effect of pre-deformation on hydrogen diffusion and hydrogen embrittlement of the high alloy austenitic TRIP steel X3CrMnNiMo17-8-4. Different cold-rolled steel sheets with thicknesses of ≤400 µm were electrochemically charged on both sides in 0.1 M sodium hydroxide with [...] Read more.
This study focuses on the effect of pre-deformation on hydrogen diffusion and hydrogen embrittlement of the high alloy austenitic TRIP steel X3CrMnNiMo17-8-4. Different cold-rolled steel sheets with thicknesses of ≤400 µm were electrochemically charged on both sides in 0.1 M sodium hydroxide with hydrogen for two weeks. Comparative measurements on uncharged and immersed samples prove that hydrogen causes embrittlement in this steel for all investigated states. The embrittlement increases with increasing pre-deformation and is accompanied by deformation-induced martensite formation. The corresponding fractured surfaces were examined using electron microscopy and compared to modelled hydrogen distributions with previously determined diffusion coefficients. For this purpose, various diffusion coefficients are determined using the Devanathan–Stachurski permeation test and hot extraction in order to describe the diffusion process. The hydrogen concentration profiles and the fractographic analyses show a good agreement, so this study provides a basis for estimating the embrittlement behaviour for later application. Full article
(This article belongs to the Special Issue Corrosion Behavior and Mechanical Properties of Metallic Materials)
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<p>(<b>a</b>) Schematic drawing of tensile test samples extracted from the hydrogen-charged area; (<b>b</b>) geometry of the used tensile samples according to [<a href="#B38-materials-17-06114" class="html-bibr">38</a>] (Unit:  mm).</p>
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<p>Schematic view of calculated hydrogen distributions in a plane sheet after hydrogen charging and subsequent discharging, grey areas indicate the integral of curves, representing the total amount of hydrogen. Black/red line—concentration profile <span class="html-italic">c</span>(x) after charging/discharging.</p>
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<p>(<b>a</b>) Hydrogen concentrations in <span class="html-italic">ε</span> = 0.49 pre-deformed X3CrMnNiMoN17-8-4 and corresponding mathematical fit using Equations (4) and (6); (<b>b</b>) calculated hydrogen distribution profiles in pre-deformed <span class="html-italic">ε</span> = 0.49 samples after different durations of charging at RT using the extrapolated equilibrium concentration <span class="html-italic">c</span><sub>1</sub> = 780 ppm and the extrapolated apparent diffusion coefficient <span class="html-italic">D<sub>app</sub></span> = 4.2 × 10<sup>−11</sup> cm<sup>2</sup> s<sup>−1</sup>.</p>
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<p>Experimentally determined hydrogen concentrations during discharging at atmosphere in <span class="html-italic">ε</span> = 0.49 pre-deformed steel sample after 36 days of hydrogen charging and corresponding mathematical fit using the extrapolated apparent diffusion coefficients <span class="html-italic">D<sub>app</sub></span> determined by DS cell (red line) and by hot extraction (blue line).</p>
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<p>Hydrogen distributions in different pre-deformed states of X3CrMnNiMoN17-8-4 after two weeks of electrochemical charging (black line) and after two weeks of discharging (red line); (<b>a</b>) <span class="html-italic">ε</span> = 0, (<b>b</b>) <span class="html-italic">ε</span> = 0.32, (<b>c</b>) <span class="html-italic">ε</span> = 0.39, and (<b>d</b>) <span class="html-italic">ε</span> = 0.49. Dashed lines indicate the sample width used for calculation.</p>
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<p>Results of tensile tests for X3CrMnNiMoN17-8-4 at different states of pre-deformation. The values of <span class="html-italic">α</span>′ provided for each curve give the initial α′ content received after cold rolling and the final <span class="html-italic">α</span>′ content determined after tensile testing.</p>
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<p>Tensile test results for X3CrMnNiMoN17-8-4 with and without hydrogen charging and after 2 weeks of immersion in 0.1 M sodium hydroxide solution with different pre-deformation; (<b>a</b>) <span class="html-italic">ε<sub>pre</sub></span> = 0, (<b>b</b>) <span class="html-italic">ε<sub>pre</sub></span> = 0.32, (<b>c</b>) <span class="html-italic">ε<sub>pre</sub></span> = 0.39, and (<b>d</b>) <span class="html-italic">ε<sub>pre</sub></span> = 0.49.</p>
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<p>Comparison of fractured surfaces after tensile testing of the X3CrMnNiMoN17-8-4 in the (<b>a</b>) uncharged state and (<b>b</b>) after two weeks of hydrogen charging.</p>
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<p>Characteristics of HE on the fracture surface of hydrogen charged X3CrMnNiMoN17-8-4 after tensile testing. (<b>a</b>) Gaping grain boundaries, (<b>b</b>) microcracks around inclusions, and (<b>c</b>) fine ductile hairlines known as “crow’s feet”.</p>
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<p>Comparison of fracture surfaces and calculated hydrogen distributions after two weeks of charging and two weeks of discharging in the samples of X3CrMnNiMoN17-8-4 at different degrees of deformation with (<b>a</b>) <span class="html-italic">ε</span> = 0, (<b>b</b>) <span class="html-italic">ε</span> = 0.32. (<b>c</b>) <span class="html-italic">ε</span> = 0.39, and (<b>d</b>) <span class="html-italic">ε</span> = 0.49.</p>
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25 pages, 1472 KiB  
Review
A Comprehensive Review of Multiple Physical and Data-Driven Model Fusion Methods for Accurate Lithium-Ion Battery Inner State Factor Estimation
by Junjie Tao, Shunli Wang, Wen Cao, Carlos Fernandez and Frede Blaabjerg
Batteries 2024, 10(12), 442; https://doi.org/10.3390/batteries10120442 - 13 Dec 2024
Viewed by 499
Abstract
With the rapid global growth in demand for renewable energy, the traditional energy structure is accelerating its transition to low-carbon, clean energy. Lithium-ion batteries, due to their high energy density, long cycle life, and high efficiency, have become a core technology driving this [...] Read more.
With the rapid global growth in demand for renewable energy, the traditional energy structure is accelerating its transition to low-carbon, clean energy. Lithium-ion batteries, due to their high energy density, long cycle life, and high efficiency, have become a core technology driving this transformation. In lithium-ion battery energy storage systems, precise state estimation, such as state of charge, state of health, and state of power, is crucial for ensuring system safety, extending battery lifespan, and improving energy efficiency. Although physics-based state estimation techniques have matured, challenges remain regarding accuracy and robustness in complex environments. With the advancement of hardware computational capabilities, data-driven algorithms are increasingly applied in battery management, and multi-model fusion approaches have emerged as a research hotspot. This paper reviews the fusion application between physics-based and data-driven models in lithium-ion battery management, critically analyzes the advantages, limitations, and applicability of fusion models, and evaluates their effectiveness in improving state estimation accuracy and robustness. Furthermore, the paper discusses future directions for improvement in computational efficiency, model adaptability, and performance under complex operating conditions, aiming to provide theoretical support and practical guidance for developing lithium-ion battery management technologies. Full article
(This article belongs to the Section Battery Modelling, Simulation, Management and Application)
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<p>Flowchart of model-based state estimation.</p>
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<p>Common types of equivalent circuit models. (<b>a</b>) Randles ECM; (<b>b</b>) Thevenin ECM; (<b>c</b>) PNGV ECM; (<b>d</b>) Second-order RC ECM; (<b>e</b>) Fractional-order ECM.</p>
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<p>Schematic diagrams of the SPM and P2D model. (<b>a</b>) Single particle model; (<b>b</b>) Pseudo-2D model.</p>
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<p>Flowchart of state estimation based on data-driven models.</p>
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17 pages, 6521 KiB  
Article
Rational Fabrication of Ag2S/g-C3N4 Heterojunction for Photocatalytic Degradation of Rhodamine B Dye Under Natural Solar Radiation
by Ali Alsalme, Ahmed Najm, Nagy N. Mohammed, M. F. Abdel Messih, Ayman Sultan and Mohamed Abdelhay Ahmed
Catalysts 2024, 14(12), 914; https://doi.org/10.3390/catal14120914 - 11 Dec 2024
Viewed by 578
Abstract
Near-infrared light-triggered photocatalytic water treatment has attracted significant attention in recent years. In this novel research, rational sonochemical fabrication of Ag2S/g-C3N4 nanocomposites with various compositions of Ag2S (0–25) wt% was carried out to eliminate hazardous rhodamine [...] Read more.
Near-infrared light-triggered photocatalytic water treatment has attracted significant attention in recent years. In this novel research, rational sonochemical fabrication of Ag2S/g-C3N4 nanocomposites with various compositions of Ag2S (0–25) wt% was carried out to eliminate hazardous rhodamine B dye in a cationic organic pollutant model. g-C3N4 sheets were synthesized via controlled thermal annealing of microcrystalline urea. However, black Ag2S nanoparticles were synthesized through a precipitation-assisted sonochemical route. The chemical interactions between various compositions of Ag2S and g-C3N4 were carried out in an ultrasonic bath with a power of 300 W. XRD, PL, DRS, SEM, HRTEM, mapping, BET, and SAED analysis were used to estimate the crystalline, optical, nanostructure, and textural properties of the solid specimens. The coexistence of the diffraction peaks of g-C3N4 and Ag2S implied the successful production of Ag2S/g-C3N4 heterojunctions. The band gap energy of g-C3N4 was exceptionally reduced from 2.81 to 1.5 eV with the introduction of 25 wt% of Ag2S nanoparticles, implying the strong absorbability of the nanocomposites to natural solar radiation. The PL signal intensity of Ag2S/g-C3N4 was reduced by 40% compared with pristine g-C3N4, implying that Ag2S enhanced the electron–hole transportation and separation. The rate of the photocatalytic degradation of rhodamine B molecules was gradually increased with the introduction of Ag2S on the g-C3N4 surface and reached a maximum for nanocomposites containing 25 wt% Ag2S. The radical trapping experiments demonstrated the principal importance of reactive oxygen species and hot holes in destroying rhodamine B under natural solar radiation. The charge transportation between Ag2S and g-C3N4 semiconductors proceeded through the type I straddling scheme. The enriched photocatalytic activity of Ag2S/g-C3N4 nanocomposites resulted from an exceptional reduction in band gap energy and controlling the electron–hole separation rate with the introduction of Ag2S as an efficient photothermal photocatalyst. The novel as-synthesized nanocomposites are considered a promising photocatalyst for destroying various types of organic pollutants under low-cost sunlight radiation. Full article
(This article belongs to the Section Photocatalysis)
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<p>XRD of g-C<sub>3</sub>N<sub>4</sub>, Ag<sub>2</sub>S, and CNAgS25 nanocomposites.</p>
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<p>N<sub>2</sub>-adsorption isotherm of (<b>a</b>) g-C<sub>3</sub>N<sub>4</sub> and (<b>b</b>) CNAgS25.</p>
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<p>(<b>a</b>) SEM of CNAgS25, (<b>b</b>) mapping of CNAgS25, (<b>c</b>) mapping of C, (<b>d</b>) mapping of (N), (<b>e</b>) mapping of Ag, (<b>f</b>) mapping of S, (<b>g</b>) EDX of CNAgS25.</p>
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<p>(<b>a</b>) TEM of CNAgS25, (<b>b</b>) HRTEM of CNAgS25 and (<b>c</b>) SAED of CNAgS25.</p>
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<p>(<b>a</b>) TEM of CNAgS25, (<b>b</b>) HRTEM of CNAgS25 and (<b>c</b>) SAED of CNAgS25.</p>
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<p>(<b>a</b>) DRS of g-C<sub>3</sub>N<sub>4</sub>, Ag<sub>2</sub>S, CNAgS15, and CNAgS25. (<b>b</b>) Tauc plot of g-C<sub>3</sub>N<sub>4</sub>, Ag2S, CNAgS15, and CNAgS25.</p>
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<p>PL analysis of g-C<sub>3</sub>N<sub>4</sub>, NAgS15, and CNAgS25.</p>
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<p>The absorption spectrum for photocatalytic degradation of rhodamine B over the surfaces of g-C3N4, CNAg10, CNAg15, and CNAg25.</p>
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<p>(<b>a</b>) The variations in the amount of RhB removed (%) under dark and light reactions with the illumination time over the surfaces of g-C<sub>3</sub>N<sub>4</sub>, CNAg10, CNAg15, and CNAg25. (<b>b</b>) The kinetic first-order plot for photocatalytic degradation of RhB dye over the surfaces of g-C<sub>3</sub>N<sub>4</sub>, CNAg10, CNAg15, and CNAg25.</p>
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<p>Photocatalytic degradation of rhodamine B (2 × 10<sup>−5</sup> M) over CNAgS25 nanocomposite in the presence of 2 × 10<sup>−5</sup> M of the following scavengers: (<b>a</b>) benzoquinone, (<b>b</b>) ammonium oxalate, and (<b>c</b>) isopropanol. (<b>d</b>) PL spectrum of terephthalic acid 2 × 10<sup>−4</sup> M over CNAgS25 nanocomposite at 325 nm excitation wavelength.</p>
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<p>Photocatalytic degradation of rhodamine B (2 × 10<sup>−5</sup> M) over CNAgS25 nanocomposite in the presence of 2 × 10<sup>−5</sup> M of the following scavengers: (<b>a</b>) benzoquinone, (<b>b</b>) ammonium oxalate, and (<b>c</b>) isopropanol. (<b>d</b>) PL spectrum of terephthalic acid 2 × 10<sup>−4</sup> M over CNAgS25 nanocomposite at 325 nm excitation wavelength.</p>
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<p>Regeneration of CNAgS25 for five consecutive cycles for removal of RhB dye over CNAgS25 nanocomposite.</p>
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<p>A scheme for electron transportation between g-C<sub>3</sub>N<sub>4</sub> and Ag<sub>2</sub>S semiconductors.</p>
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<p>Scheme for synthesis of (<b>a</b>) g-C<sub>3</sub>N<sub>4</sub>, (<b>b</b>) Ag<sub>2</sub>S and (<b>c</b>) Ag<sub>2</sub>S/g-C<sub>3</sub>N<sub>4</sub> heterojunction.</p>
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24 pages, 5781 KiB  
Article
Co-Design Optimization and Total Cost of Ownership Analysis of an Electric Bus Depot Microgrid with Photovoltaics and Energy Storage Systems
by Boud Verbrugge, Thomas Geury and Omar Hegazy
Energies 2024, 17(24), 6233; https://doi.org/10.3390/en17246233 - 11 Dec 2024
Viewed by 361
Abstract
Due to the increasing share of battery electric buses (BEBs) in cities, depots need to be adapted to the increasing load demand. The integration of renewable energy sources (RESs) into a depot can increase the self-consumption, but optimal sizing is required for a [...] Read more.
Due to the increasing share of battery electric buses (BEBs) in cities, depots need to be adapted to the increasing load demand. The integration of renewable energy sources (RESs) into a depot can increase the self-consumption, but optimal sizing is required for a cost-efficient and reliable operation. Accordingly, this paper introduces a co-design optimization framework for a depot microgrid, equipped with photovoltaics (PVs) and an energy storage system (ESS). Three European cities are considered to evaluate the effect of different environmental conditions and electricity prices on the optimal microgrid design. Accurate models of the different subsystems are created to estimate the load demand and the power generation. Different energy management strategies (EMSs), developed to properly control the power flow within the microgrid, are compared in terms of operational costs reduction, one of which was also experimentally validated using a hardware-in-the-loop (HiL) test setup. In addition, the total cost of ownership (TCO) of the depot microgrid is analyzed, showing that an optimally designed depot microgrid can reduce the charging-related expenses for the public transport operator (PTO) by 30% compared to a scenario in which only the distribution grid supplies the BEB depot. Full article
(This article belongs to the Section E: Electric Vehicles)
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<p>Overview of the architecture of the depot microgrid.</p>
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<p>Single-diode model of a PV module.</p>
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<p>Equivalent circuit diagram of a first-order Thevenin model.</p>
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<p>Overview of the control signals of the simple EMS (all, except tariff) and the advanced EMS (all).</p>
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<p>Flowchart of the advanced rule-based EMS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Brussels with the simple EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Barcelona with the simple EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Gothenburg with the simple EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Brussels with the advanced EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Barcelona with the advanced EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>Simulation results illustrating the operation of the depot microgrid in Gothenburg with the advanced EMS with (<b>a</b>) electricity tariff, (<b>b</b>) current of each subsystem, and (<b>c</b>) SoC of the ESS.</p>
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<p>TCO comparison of different depot configurations in the considered cities.</p>
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<p>Overview of the power devices included in the HiL test setup to represent the depot microgrid.</p>
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<p>HiL test setup of a depot microgrid.</p>
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<p>Experimental test results of the EMS for the DC microgrid with (<b>a</b>) electricity tariff and (<b>b</b>) current of each subsystem.</p>
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16 pages, 781 KiB  
Article
A Comparative Study of Electric Vehicles Battery State of Charge Estimation Based on Machine Learning and Real Driving Data
by Salma Ariche, Zakaria Boulghasoul, Abdelhafid El Ouardi, Abdelhadi Elbacha, Abdelouahed Tajer and Stéphane Espié
J. Low Power Electron. Appl. 2024, 14(4), 59; https://doi.org/10.3390/jlpea14040059 - 11 Dec 2024
Viewed by 604
Abstract
Electric vehicles (EVs) are rising in the automotive industry, replacing combustion engines and increasing their global market presence. These vehicles offer zero emissions during operation and more straightforward maintenance. However, for such systems that rely heavily on battery capacity, precisely determining the battery’s [...] Read more.
Electric vehicles (EVs) are rising in the automotive industry, replacing combustion engines and increasing their global market presence. These vehicles offer zero emissions during operation and more straightforward maintenance. However, for such systems that rely heavily on battery capacity, precisely determining the battery’s state of charge (SOC) presents a significant challenge due to its essential role in lithium-ion batteries. This research introduces a dual-phase testing approach, considering factors like HVAC use and road topography, and evaluating machine learning models such as linear regression, support vector regression, random forest regression, and neural networks using datasets from real-world driving conditions in European (Germany) and African (Morocco) contexts. The results validate that the proposed neural networks model does not overfit when evaluated using the dual-phase test method compared to previous studies. The neural networks consistently show high predictive precision across different scenarios within the datasets, outperforming other models by achieving the lowest mean squared error (MSE) and the highest R2 values. Full article
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<p>BEV model with powertrain and thermal management system.</p>
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<p>Flow chart of the proposed data-driven methods to estimate battery SOC.</p>
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<p>NN architecture with selected features for each driving scenario ((<b>a</b>) Munich20, (<b>b</b>) HELECAR-D 2).</p>
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<p>Recorded SOC vs. Estimated SOCusing Munich20.</p>
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<p>Recorded SOC vs. Estimated SOC using HELECAR-D.</p>
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<p>Recorded SOC vs. NN-Estimated SOC using Munich20.</p>
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<p>Recorded SOC vs. NN-Estimated SOC using HELECAR-D.</p>
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34 pages, 5942 KiB  
Article
Gold Recovery from Smelting Copper Sulfide Concentrate
by Elmira Moosavi-Khoonsari and Nagendra Tripathi
Processes 2024, 12(12), 2795; https://doi.org/10.3390/pr12122795 - 7 Dec 2024
Viewed by 580
Abstract
Gold is a significant revenue source for custom copper smelters facing profitability challenges due to low treatment and refining charges, stricter regulations, and rising costs. Gold is also often blended with copper concentrates, but precise recovery rates from smelting processes are poorly documented [...] Read more.
Gold is a significant revenue source for custom copper smelters facing profitability challenges due to low treatment and refining charges, stricter regulations, and rising costs. Gold is also often blended with copper concentrates, but precise recovery rates from smelting processes are poorly documented despite gold critical economic importance. This paper aims to provide the first comprehensive estimates of gold first-pass recovery across various operational units within the copper sulfide concentrate processing flowsheet. It evaluates the effectiveness of different copper smelting and converting technologies in recovering gold. Optimizing gold first-pass recovery is especially important to enhance immediate financial returns and responsiveness to market dynamics, allowing companies to capitalize on favorable gold prices without delays. Given the absence of direct measurements for gold recovery rates, this research develops an estimation method based on understanding gold loss mechanisms during smelting. This study identifies and analyzes key input and output parameters by examining data from various copper producers. By correlating these parameters with gold loss, the research estimates gold first-pass recovery rates within the copper smelting process. Among integrated smelting-converting routes, the flash smelting to Peirce–Smith converting route achieves the highest gold first-pass recovery (98.8–99.5%), followed by the Mitsubishi continuous smelting and converting process (94.3–99.8%), bottom-blowing smelting to bottom-blowing converting (95.8%), flash smelting to flash converting (95.5%), Teniente smelting to Peirce–Smith converting (95.2%), and the Noranda continuous smelting and converting process (94.8%). The final recovery rates are expected to be higher considering the by-products’ internal recirculation and post-processing within the copper flow sheet. Additionally, superior gold recoveries are attributed to advanced metallurgical practices and control systems, which vary even among companies with similar technologies. This research demonstrates that copper smelting can effectively recover over 99% of gold from sulfide concentrates. Gold accumulates up to 1000 times its original concentration in anode slime during electrolytic refining, generating 5–10 kg of slime per ton of copper, which is further processed to recover gold and other by-products. Major smelters operate precious metal plants where recovering gold from highly concentrated anode slime is both cost-effective and efficient. Full article
(This article belongs to the Special Issue Recent Trends in Extractive Metallurgy)
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<p>Treatment charges (TCs) of copper concentrate from 2019 to 2024, along with the corresponding annual benchmark rates (data from Fastmarkets analysis [<a href="#B1-processes-12-02795" class="html-bibr">1</a>]).</p>
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<p>Breakdown of global copper production in 2023, highlighting the share of mined and recycled copper and the distribution of smelting methods (data from [<a href="#B10-processes-12-02795" class="html-bibr">10</a>]).</p>
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<p>World copper production by origin in 2022 (top 20 countries): (<b>a</b>) mine and (<b>b</b>) smelter (data from [<a href="#B10-processes-12-02795" class="html-bibr">10</a>]).</p>
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<p>China’s copper concentrate imports by origin in 2023 (in million tons) (data from [<a href="#B14-processes-12-02795" class="html-bibr">14</a>]).</p>
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<p>Overview of copper-making flowsheet.</p>
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<p>Gold payables for different gold grades in a copper concentrate in the Japanese market.</p>
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<p>Gold partition coefficient between matte and slag versus Cu concentration in matte. [20Che]: 1300 °C, 0.1 atm SO<sub>2</sub>, ICP [<a href="#B43-processes-12-02795" class="html-bibr">43</a>]; [16Ava]: 0.1 atm SO<sub>2</sub>, FS, EPMA [<a href="#B6-processes-12-02795" class="html-bibr">6</a>]; [15Ava]: 0.1 atm SO<sub>2</sub>, FS slag, ICP [<a href="#B5-processes-12-02795" class="html-bibr">5</a>]; [06Hen]: 0.1 atm SO<sub>2</sub>, FSM slag, ICP-MS [<a href="#B44-processes-12-02795" class="html-bibr">44</a>]. F, S, M, A, and C stand for FeO, SiO<sub>2</sub>, MgO, Al<sub>2</sub>O<sub>3</sub>, and CaO in slag.</p>
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<p>Gold partition coefficients between copper and slag versus oxygen partial pressure. Experimental data were obtained for alumina-saturated iron silicate slag using LA-ICP-MS (data from [<a href="#B7-processes-12-02795" class="html-bibr">7</a>]).</p>
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<p>Gold partition coefficients between copper and matte (diamond) and copper and white metal (square) versus temperature [<a href="#B4-processes-12-02795" class="html-bibr">4</a>,<a href="#B54-processes-12-02795" class="html-bibr">54</a>].</p>
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<p>Gold concentrations (in log<sub>10</sub> in ppm) in several phases in copper anode electro-refining [<a href="#B30-processes-12-02795" class="html-bibr">30</a>,<a href="#B67-processes-12-02795" class="html-bibr">67</a>]. CAS represents copper anode slime.</p>
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<p>Production shares of different copper smelting technologies. TSL and SKS stand for top submerged lance and Shuangyashan Kiln Stove, respectively (data from [<a href="#B71-processes-12-02795" class="html-bibr">71</a>]).</p>
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<p>Liquidus temperatures of iron silicate slags versus Fe/SiO<sub>2</sub> weight ratio in bulk slag. Lines from FactSage 8.3 FToxid for different <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>P</mi> </mrow> <mrow> <msub> <mrow> <mi>O</mi> </mrow> <mrow> <mn>2</mn> </mrow> </msub> </mrow> </msub> </mrow> </semantics></math> (in atm) and CaO contents (in wt%), along with slag tapping temperatures of various smelting furnaces (data from [<a href="#B41-processes-12-02795" class="html-bibr">41</a>,<a href="#B43-processes-12-02795" class="html-bibr">43</a>,<a href="#B48-processes-12-02795" class="html-bibr">48</a>,<a href="#B60-processes-12-02795" class="html-bibr">60</a>,<a href="#B79-processes-12-02795" class="html-bibr">79</a>,<a href="#B80-processes-12-02795" class="html-bibr">80</a>,<a href="#B84-processes-12-02795" class="html-bibr">84</a>,<a href="#B86-processes-12-02795" class="html-bibr">86</a>]).</p>
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<p>Total copper loss to slag in wt% versus Fe/SiO<sub>2</sub> weight ratio in bulk slag for different smelting technologies (data from [<a href="#B41-processes-12-02795" class="html-bibr">41</a>,<a href="#B43-processes-12-02795" class="html-bibr">43</a>,<a href="#B60-processes-12-02795" class="html-bibr">60</a>,<a href="#B76-processes-12-02795" class="html-bibr">76</a>,<a href="#B77-processes-12-02795" class="html-bibr">77</a>,<a href="#B78-processes-12-02795" class="html-bibr">78</a>,<a href="#B79-processes-12-02795" class="html-bibr">79</a>,<a href="#B80-processes-12-02795" class="html-bibr">80</a>,<a href="#B86-processes-12-02795" class="html-bibr">86</a>,<a href="#B87-processes-12-02795" class="html-bibr">87</a>,<a href="#B88-processes-12-02795" class="html-bibr">88</a>,<a href="#B89-processes-12-02795" class="html-bibr">89</a>,<a href="#B90-processes-12-02795" class="html-bibr">90</a>,<a href="#B91-processes-12-02795" class="html-bibr">91</a>,<a href="#B92-processes-12-02795" class="html-bibr">92</a>,<a href="#B93-processes-12-02795" class="html-bibr">93</a>,<a href="#B94-processes-12-02795" class="html-bibr">94</a>]).</p>
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<p>Copper physical loss in slag (in wt%) for several converters. Peirce–Smith converters (PSC: Aurubis, Boliden, Codelco, Hibi Kyodo, Sumitomo, Pan Pacific, and Unknown), Flash converter (FC: Rio Tinto Kennecott), Noranda converter (Horne), Mitsubishi converters (Naoshima, Gresik, and Onsan), Teniente converters (Chuquicamata, Unknown 2, Unknown 3, Hernan Videla Vira, and Potrerillos), bottom-blowing converter (BBC: Baotou and Dongying Phase II) (data from [<a href="#B68-processes-12-02795" class="html-bibr">68</a>,<a href="#B69-processes-12-02795" class="html-bibr">69</a>,<a href="#B81-processes-12-02795" class="html-bibr">81</a>,<a href="#B90-processes-12-02795" class="html-bibr">90</a>,<a href="#B91-processes-12-02795" class="html-bibr">91</a>,<a href="#B92-processes-12-02795" class="html-bibr">92</a>,<a href="#B93-processes-12-02795" class="html-bibr">93</a>]).</p>
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<p>Gold first-pass recovery (in %) calculated in this work for different smelting and converting technologies (smelting: blue and converting: orange).</p>
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24 pages, 11173 KiB  
Article
Advanced State-of-Health Estimation for Lithium-Ion Batteries Using Multi-Feature Fusion and KAN-LSTM Hybrid Model
by Zhao Zhang, Runrun Zhang, Xin Liu, Chaolong Zhang, Gengzhi Sun, Yujie Zhou, Zhong Yang, Xuming Liu, Shi Chen, Xinyu Dong, Pengyu Jiang and Zhexuan Sun
Batteries 2024, 10(12), 433; https://doi.org/10.3390/batteries10120433 - 6 Dec 2024
Viewed by 613
Abstract
Accurate assessment of battery State of Health (SOH) is crucial for the safe and efficient operation of electric vehicles (EVs), which play a significant role in reducing reliance on non-renewable energy sources. This study introduces a novel SOH estimation method combining Kolmogorov–Arnold Networks [...] Read more.
Accurate assessment of battery State of Health (SOH) is crucial for the safe and efficient operation of electric vehicles (EVs), which play a significant role in reducing reliance on non-renewable energy sources. This study introduces a novel SOH estimation method combining Kolmogorov–Arnold Networks (KAN) and Long Short-Term Memory (LSTM) networks. The method is based on fully charged battery characteristics, extracting key parameters such as voltage, temperature, and charging data collected during cycles. Validation was conducted under a temperature range of 10 °C to 30 °C and different charge–discharge current rates. Notably, temperature variations were primarily caused by seasonal changes, enabling the experiments to more realistically simulate the battery’s performance in real-world applications. By enhancing dynamic modeling capabilities and capturing long-term temporal associations, experimental results demonstrate that the method achieves highly accurate SOH estimation under various charging conditions, with low mean absolute error (MAE) and root mean square error (RMSE) values and a coefficient of determination (R2) exceeding 97%, significantly improving prediction accuracy and efficiency. Full article
(This article belongs to the Special Issue Control, Modelling, and Management of Batteries)
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<p>Experimental equipment diagram.</p>
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<p>Voltage and current curves while charging.</p>
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<p>Variation of voltage curve with charging times in constant current charging state.</p>
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<p>Characteristic pattern. (<b>a</b>) Constant current charging time; (<b>b</b>) The amount of electricity charged at constant voltage; (<b>c</b>) Constant-voltage charging time; (<b>d</b>) Integral of temperature.</p>
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<p>Curve of current versus charging times in constant-voltage charging state.</p>
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<p>Relational graph.</p>
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<p>KAN model structure.</p>
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<p>LSTM Model Structure.</p>
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<p>Flow chart of the experimental steps.</p>
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<p>The curve of SOH versus the number of charging times.</p>
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<p>Graph of the prediction results of the KAN-LSTM model.</p>
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<p>Comparison of the prediction results of each model.</p>
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<p>The curve of average temperature versus the number of charging times.</p>
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<p>Figure of the prediction results of the KAN-LSTM model under the condition of missing temperature features.</p>
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<p>Model performance on the NASA dataset.</p>
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<p>Model performance on the NASA dataset.</p>
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<p>Prediction results across batteries at different charging rates.</p>
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10 pages, 1275 KiB  
Article
Ab Initio Study of the β-Fe2O3 Phase
by Priyanka Mishra and Carmine Autieri
Molecules 2024, 29(23), 5751; https://doi.org/10.3390/molecules29235751 - 5 Dec 2024
Viewed by 496
Abstract
We present first-principles results on the electronic and magnetic properties of the cubic bulk β-phase of Fe2O3. Given that all Fe–Fe magnetic couplings are expected to be antiferromagnetic within this high-symmetry crystal structure, the system may exhibit some [...] Read more.
We present first-principles results on the electronic and magnetic properties of the cubic bulk β-phase of Fe2O3. Given that all Fe–Fe magnetic couplings are expected to be antiferromagnetic within this high-symmetry crystal structure, the system may exhibit some signature of magnetic frustration, making it challenging to identify its magnetic ground state. We have analyzed the possible magnetic phases of the β-phase, among which there are ferrimagnets, altermagnets, and Kramers antiferromagnets. While the α-phase is an altermagnet and the γ-phase is a ferrimagnet, we conclude that the magnetic ground state for the bulk β-phase of Fe2O3 is a Kramers antiferromagnet. Moreover, we find that close in energy, there is a bulk d-wave altermagnetic phase. We report the density of states and the evolution band gap as a function of the electronic correlations. For suitable values of the Coulomb repulsion, the system is a charge-transfer insulator with an indirect band gap of 1.5 eV. More in detail, the unit cell of the β-phase is composed of 8Fea atoms and 24Feb atoms. The 8Fea atoms lie on the corner of a cube, and their magnetic ground state is a G-type. This structural phase is composed of zig-zag chains FeaFebFeaFeb with spin configuration ↑-↑-↓-↓ along the 3 directions such that for every Fea atoms there are 3Feb atoms. As the opposite to the γ-phase, the magnetic configuration between the first neighbor of the same kind is always antiferromagnetic while the magnetic configuration between Fea and Feb is ferro or antiferro. In this magnetic arrangement, first-neighbor interactions cancel out in the mean-field estimation of the Néel temperature, leaving second-neighbor magnetic exchanges as the primary contributors, resulting in a Néel temperature lower than that of other phases. Our work paves the way toward the ab initio study of nanoparticles and alloys for the β-phase of Fe2O3. Full article
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Figure 1
<p>Crystal structure of the <math display="inline"><semantics> <mi>β</mi> </semantics></math><math display="inline"><semantics> <mrow> <mo>‐</mo> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math> phase. The <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math>, and oxygen atoms are represented by blue, brown, and red balls, respectively. (<b>a</b>) The system presents two kinds of <math display="inline"><semantics> <mrow> <msub> <mi>FeO</mi> <mn>6</mn> </msub> </mrow> </semantics></math> octahedra which are <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>6</mn> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>6</mn> </msub> </mrow> </semantics></math> represented in blue and brown, respectively. (<b>b</b>) There are <math display="inline"><semantics> <mrow> <mn>8</mn> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>6</mn> </msub> </mrow> </mrow> </semantics></math> octahedra, which are centered at the high-symmetry positions (0.50 ± 0.25a, 0.50 ± 0.25a, 0.50 ± 0.25a) where a is the lattice constant.</p>
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<p>Slice of the zig-zag connectivity of the <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms in the <math display="inline"><semantics> <mi>β</mi> </semantics></math><math display="inline"><semantics> <mrow> <mo>‐</mo> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math> phase. (<b>a</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms at direct coordinate z = 0.25. (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms at the direct coordinate z = 0.75. Given the cubic symmetry, the same connectivity is present for slices in all the equivalent directions. The <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> and oxygen atoms are represented by brown and blue, respectively. The oxygen atoms are not shown.</p>
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<p>Inequivalent magnetic configurations of the <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> atoms with zero net magnetic moment for a cubic system. The antiferromagnetic configurations are usually named (<b>a</b>) A-type, (<b>b</b>) C-type, (<b>c</b>) F-type and (<b>d</b>) G-type. The <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms are shown as black balls, while the red and blue arrows represent the spin-up and spin-down, respectively.</p>
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<p>(<b>a</b>) Energy differences per formula units and (<b>b</b>) evolution of the band gap as a function of the Coulomb repulsion U for the magnetic configurations closer to the ground state of the bulk <math display="inline"><semantics> <mi>β</mi> </semantics></math><math display="inline"><semantics> <mrow> <mo>‐</mo> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math>. The Coulomb repulsion ranges from 0 to 6 eV. (<b>a</b>) <math display="inline"><semantics> <mo>Δ</mo> </semantics></math><math display="inline"><semantics> <mrow> <msub> <mi mathvariant="normal">E</mi> <mn>1</mn> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mo>Δ</mo> </semantics></math><math display="inline"><semantics> <mrow> <msub> <mi mathvariant="normal">E</mi> <mn>2</mn> </msub> </mrow> </semantics></math> are represented with solid red and blue, respectively. (<b>b</b>) The gap of the magnetic ground is plotted in dotted green. The second and third magnetic states in energy are plotted in dashed red and solid blue, respectively.</p>
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<p>(<b>a</b>) Total and atomic-resolved DOS for the magnetic ground state of the <math display="inline"><semantics> <mi>β</mi> </semantics></math>-phase. Total DOS per Fe atoms of the <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math> are plotted in black. The majority of d-electrons of <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> spin are plotted in red and blue, respectively. Minority d-electrons of <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> spin are plotted in green and pink, respectively. (<b>b</b>) Band structure of the magnetic ground state with an indirect band gap. The top of the valence band is at the <math display="inline"><semantics> <mo>Γ</mo> </semantics></math> point, while the bottom of the conduction band is indicated by the orange arrow and placed along the <math display="inline"><semantics> <mo>Γ</mo> </semantics></math>-R k-path. The band structure is double degenerate due to the Kramers degeneracy.</p>
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<p>Total and atomic-resolved DOS for the (<b>a</b>) second and (<b>b</b>) third-lowest energy state of the <math display="inline"><semantics> <mi>β</mi> </semantics></math>-phase. Total DOS per Fe atoms of the <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math> are plotted in black. The majority of d-electrons of <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> spin are plotted in red and blue, respectively. Minority d-electrons of <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> spin are plotted in green and pink, respectively.</p>
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<p>Real-space magnetic configuration of the ground state for the slices at (<b>a</b>) z = 0.25 and (<b>b</b>) z = 0.75. <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms are blue and brown, respectively. Spin-up and spin-down are red and blue, respectively.</p>
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<p>Main exchange couplings for the <math display="inline"><semantics> <mi>β</mi> </semantics></math>-phase of <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mn>2</mn> </msub> <msub> <mi mathvariant="normal">O</mi> <mn>3</mn> </msub> </mrow> </semantics></math>. The only first-neighbor coupling is <math display="inline"><semantics> <mrow> <msub> <mi mathvariant="normal">J</mi> <mrow> <mi>F</mi> <msub> <mi>e</mi> <mi>a</mi> </msub> <mo>−</mo> <mi>F</mi> <msub> <mi>e</mi> <mi>b</mi> </msub> </mrow> </msub> </mrow> </semantics></math>. Regarding the second-neighbor couplings, these are between atoms of the same kind, which can be interchain (inter) or intrachain (intra). Due to the structural properties, the interchain and intrachain coupling are equivalent for <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>a</mi> </msub> </mrow> </semantics></math> atoms but not for <math display="inline"><semantics> <mrow> <msub> <mi>Fe</mi> <mi>b</mi> </msub> </mrow> </semantics></math> atoms. Therefore, we have <math display="inline"><semantics> <mrow> <msub> <mi mathvariant="normal">J</mi> <mrow> <mi>F</mi> <msub> <mi>e</mi> <mi>a</mi> </msub> <mo>−</mo> <mi>F</mi> <msub> <mi>e</mi> <mi>a</mi> </msub> </mrow> </msub> </mrow> </semantics></math>, <math display="inline"><semantics> <mrow> <msubsup> <mi mathvariant="normal">J</mi> <mrow> <mi>F</mi> <msub> <mi>e</mi> <mi>b</mi> </msub> <mo>−</mo> <mi>F</mi> <msub> <mi>e</mi> <mi>b</mi> </msub> </mrow> <mrow> <mi>i</mi> <mi>n</mi> <mi>t</mi> <mi>e</mi> <mi>r</mi> </mrow> </msubsup> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msubsup> <mi mathvariant="normal">J</mi> <mrow> <mi>F</mi> <msub> <mi>e</mi> <mi>b</mi> </msub> <mo>−</mo> <mi>F</mi> <msub> <mi>e</mi> <mi>b</mi> </msub> </mrow> <mrow> <mi>i</mi> <mi>n</mi> <mi>t</mi> <mi>r</mi> <mi>a</mi> </mrow> </msubsup> </mrow> </semantics></math>.</p>
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23 pages, 12257 KiB  
Article
Optimal Charging Current Protocol with Multi-Stage Constant Current Using Dandelion Optimizer for Time-Domain Modeled Lithium-Ion Batteries
by Seongik Han
Appl. Sci. 2024, 14(23), 11320; https://doi.org/10.3390/app142311320 - 4 Dec 2024
Viewed by 486
Abstract
This study utilized a multi-stage constant current (MSCC) charge protocol to identify the optimal current pattern (OCP) for effectively charging lithium-ion batteries (LiBs) using a Dandelion optimizer (DO). A Thevenin equivalent circuit model (ECM) was implemented to simulate an actual LiB with the [...] Read more.
This study utilized a multi-stage constant current (MSCC) charge protocol to identify the optimal current pattern (OCP) for effectively charging lithium-ion batteries (LiBs) using a Dandelion optimizer (DO). A Thevenin equivalent circuit model (ECM) was implemented to simulate an actual LiB with the ECM parameters estimated from the offline time response data obtained through a hybrid pulse power characterization (HPPC) test. For the first time, DO was applied to metaheuristic optimization algorithms (MOAs) to determine the OCP within the MSCC protocol. A composite objective function that incorporates both charging time and charging temperature was constructed to facilitate the use of DO in obtaining the OCP. To verify the performance of the proposed method, various algorithms, including the constant current-constant voltage (CC-CV) technique, formula method (FM), particle swarm optimization (PSO), war strategy optimization (WSO), jellyfish search algorithm (JSA), grey wolf optimization (GWO), beluga whale optimization (BWO), levy flight distribution algorithm (LFDA), and African gorilla troops optimizer (AGTO), were introduced. Based on the OCP extracted from the simulations using these MOAs for the specified ECM model, a charging experiment was conducted on the Panasonic NCR18650PF LiB to evaluate the charging performance in terms of charging time, temperature, and efficiency. The results demonstrate that the proposed DO technique offers superior charging performance compared to other charging methods. Full article
(This article belongs to the Section Energy Science and Technology)
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Figure 1
<p>Thevenin equivalent circuit model, where <math display="inline"><semantics> <mrow> <msub> <mi>R</mi> <mn>0</mn> </msub> </mrow> </semantics></math> denotes the internal resistance, <math display="inline"><semantics> <mrow> <msub> <mi>R</mi> <mi>p</mi> </msub> </mrow> </semantics></math> and <math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>p</mi> </msub> </mrow> </semantics></math> represent the polarization resistance and capacitance, respectively, which characterize the rapid electrode reaction to the battery, and <math display="inline"><semantics> <mrow> <msub> <mi>C</mi> <mi>b</mi> </msub> </mrow> </semantics></math> indicates the battery capacitance. The equivalent internal resistance is defined by <math display="inline"><semantics> <mrow> <msub> <mi>R</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> <mo>=</mo> <msub> <mi>R</mi> <mn>0</mn> </msub> <mo>+</mo> <msub> <mi>R</mi> <mi>p</mi> </msub> </mrow> </semantics></math>.</p>
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<p>Experimental battery platform.</p>
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<p>Current pulse charge/discharge variations.</p>
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<p>HPPC experimental voltage curves. (<b>a</b>) Pulse power tests. (<b>b</b>) A single pulse power test.</p>
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<p>Identified characteristic curves. (<b>a</b>) OCV vs. SOC. (<b>b</b>) <math display="inline"><semantics> <mrow> <msub> <mi>R</mi> <mn>0</mn> </msub> <mo>,</mo> <mo> </mo> <mo> </mo> <msub> <mi>R</mi> <mi>p</mi> </msub> </mrow> </semantics></math>, and <math display="inline"><semantics> <mrow> <msub> <mi>R</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> </semantics></math> vs. SOC. (<b>c</b>) <math display="inline"><semantics> <mi>τ</mi> </semantics></math> vs. SOC.</p>
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<p>CC-CV charging curves. (<b>a</b>) Charging voltage (<b>b</b>) Charging current. (<b>c</b>) Charging temperature.</p>
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<p>CC-CV charging curves. (<b>a</b>) Charging voltage (<b>b</b>) Charging current. (<b>c</b>) Charging temperature.</p>
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<p>Conceptual diagram of the MSCC charging method.</p>
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<p>Dandelions in nature. (<b>a</b>) Dandelion growths. (<b>b</b>) Dandelion floating in the wind.</p>
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<p>ECM model for simulation.</p>
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<p>Charging configuration of FM. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of PSO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of WSO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of JSA. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of GWO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of BWO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of LFDA. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of AGTO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Charging configuration of DO. (<b>a</b>) Simulation. (<b>b</b>) Experiment.</p>
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<p>Experimental results for the charging temperature.</p>
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<p>Bar charts of the performance indicators. (<b>a</b>) FC. (<b>b</b>) CT. (<b>c</b>) MCT. (<b>d</b>) EL. (<b>e</b>) Total score.</p>
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