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Keywords = Ni-MH battery

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20 pages, 6706 KiB  
Article
On the Performance of Portable NiMH Batteries of General Use
by Diego F. Quintero Pulido, Catalin Felix Covrig and Matthias Bruchhausen
Batteries 2025, 11(1), 30; https://doi.org/10.3390/batteries11010030 - 16 Jan 2025
Viewed by 413
Abstract
NiMH batteries are the most used technology of rechargeable batteries sold directly to consumers. Herein, we study the performance of the most common sizes of portable NiMH batteries (AA, AAA, D, C, and 9V). The performance and durability parameters—capacity, charge retention, charge recovery, [...] Read more.
NiMH batteries are the most used technology of rechargeable batteries sold directly to consumers. Herein, we study the performance of the most common sizes of portable NiMH batteries (AA, AAA, D, C, and 9V). The performance and durability parameters—capacity, charge retention, charge recovery, and endurance in cycles—are measured for these types of batteries, according to the standard IEC 61951-2:2017 NiMH batteries. The purpose of this study is to create a basis for setting minimum performance requirements for the parameters in the European Regulation concerning batteries and waste batteries, EU 2023/1542, Annex III, Part B. Results show that the charging time of 16 h could be reduced to 8 h for verifying the rated capacity. The performance of commercial batteries with regard to charge retention, charge recovery, and endurance in cycles is often found to be 25–30% better than required in the relevant IEC standard. Furthermore, we present a short comparative analysis of an application test (IEC 60086-2:2021 “toy”) for portable NiMH batteries with primary batteries. Such data allow comparing the performance of portable NiMH batteries compared to primary batteries in the application test “toy”. Full article
(This article belongs to the Section Battery Performance, Ageing, Reliability and Safety)
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<p>Experimental facilities at JRC Petten, The Netherlands: (<b>a</b>) Maccor battery cycler with BIA temperature chambers; (<b>b</b>) Maccor battery cycler with a Vötsch temperature chamber.</p>
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<p>AA Energizer 2.5 Ah NiMH battery charge at 0.1 C and discharge at 0.2 C for different charging durations. AS = ascending charging duration; DS = descending charging duration with (<b>a</b>) charge capacity, (<b>b</b>) discharge capacity, (<b>c</b>) columbic efficiency, and (<b>d</b>) energy efficiency.</p>
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<p>NiMH battery charge profile at 0.1 C and 16 h of different battery manufacturers of (<b>a</b>) AAA, (<b>b</b>) AA, (<b>c</b>) C, (<b>d</b>) D, (<b>e</b>) rated capacity, manufacturer, size, and (<b>f</b>) average charging voltage profile.</p>
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<p>Portable NiMH batteries specific energy and internal resistance with manufacturers and designation.</p>
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<p>X-ray tomography scan cross-sectional view of AAA NiMH battery: (<b>a</b>) GP 900 mAh and (<b>b</b>) Tronic 1000 mAh rated capacity.</p>
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<p>NiMH battery discharge profiles at 0.2 C and a cut-off of 1.0 V for different battery manufacturers of (<b>a</b>) AA, (<b>b</b>) AAA, (<b>c</b>) C, (<b>d</b>) D, and (<b>e</b>) average SOC.</p>
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<p>NiMH voltage and current profiles for rated capacity analysis according to IEC 619512, for (<b>a</b>) AAA GP, (<b>b</b>) AA Duracell, (<b>c</b>) C Energizer, (<b>d</b>) D Duracell and (<b>e</b>) 9V Energizer battery.</p>
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<p>NiMH charge (capacity) retention analysis according to IEC 61951-2 with the pre-charged test for (<b>a</b>) AAA Duracell, (<b>b</b>) AA Agfaphoto, (<b>c</b>) C Ansmann, (<b>d</b>) D Ansmann, and (<b>e</b>) 9V Energizer batteries.</p>
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<p>NiMH charge (capacity) recovery analysis according to IEC 61951-2 of (<b>a</b>) AAA Agfaphoto, (<b>b</b>) AA GP, (<b>c</b>) C Varta, (<b>d</b>) D GP, and (<b>e</b>) 9V Duracell batteries.</p>
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<p>NiMH endurance in cycles analysis according to IEC 61951-2 for an AAA Energizer 700 mAh battery (<b>a</b>) voltage profile, (<b>b</b>) current profile, (<b>c</b>) capacity, and d) columbic efficiency vs. cycle number. The vertical red lines in (<b>c</b>,<b>d</b>) indicate checkup cycles.</p>
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<p>Comparison of portable NiMH batteries with primary batteries (alkaline) using the “toy” application test from IEC 60086-2, including the minimum average duration value, average duration, and measured capacity for (<b>a</b>) AAA, (<b>b</b>) AA, (<b>c</b>) C, (<b>d</b>) D, and (<b>e</b>) 9V batteries.</p>
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12 pages, 2307 KiB  
Article
Role of Electrochemical Precipitation Parameters in Developing Mixed-Phase Battery-Grade Nickel Hydroxide
by Chinmaya Kumar Sarangi, G. Lilishree Achary, Tondepu Subbaiah, Raja Kishore Paramguru and Sanat Kumar Roy
Electrochem 2025, 6(1), 2; https://doi.org/10.3390/electrochem6010002 - 16 Jan 2025
Viewed by 440
Abstract
There is a high demand for nickel hydroxide as an engineering material used in the positive electrode of nickel metal hydride (Ni-MH) rechargeable batteries. These batteries are extensively used in various small instruments, disposable batteries, and electric vehicles. The structure of nickel hydroxide [...] Read more.
There is a high demand for nickel hydroxide as an engineering material used in the positive electrode of nickel metal hydride (Ni-MH) rechargeable batteries. These batteries are extensively used in various small instruments, disposable batteries, and electric vehicles. The structure of nickel hydroxide significantly influences the discharge capacity and energy density, key properties of Ni-MH batteries, and this structure is primarily determined by the synthesis method used. In this study, nickel hydroxide was synthesized using an electrochemical precipitation method, with current density acting as a parameter to control the desired phase of the product, whether α-nickel hydroxide, β-nickel hydroxide, or a combination of both. At a current density of 50 A/m2, the synthesized nickel hydroxide demonstrated a smaller particle size and a superior discharge electrochemical property in comparison to that generated at 500 A/m2. The effect of agitation in catholyte was also investigated to examine the change in discharge property of the precipitated material. The product synthesized at 500 A/m2 from an agitated catholyte exhibited a tap density of 1.24 g/cc and an improved discharge capacity of 254 mAh per gram of Ni(OH)2. Full article
(This article belongs to the Special Issue Feature Papers in Electrochemistry)
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<p>Changes in (a) current efficiency and (b) energy consumption while increasing nickel concentration in the electrolytic bath.</p>
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<p>The relationship between increasing current density and its effects on (a) current efficiency and (b) energy consumption during the electrochemical formation of nickel hydroxide.</p>
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<p>Discharge capacity of nickel hydroxide synthesized electrochemically at varied current densities (a) 50, (b) 200, and (c) 500 A/m<sup>2</sup> without agitation in the bath.</p>
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<p>XRD patterns of nickel hydroxide synthesized electrochemically at various cathodic current densities: (a) 50 A/m<sup>2</sup>, (b) 200 A/m<sup>2</sup>, (c) 500 A/m<sup>2</sup>.</p>
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<p>XRD pattern representing a standard β-Ni(OH)<sub>2</sub> product.</p>
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<p>XRD pattern of nickel hydroxide synthesized at current density of 500 A/m<sup>2</sup> (a) without agitation and (b) with agitation in the catholyte bath.</p>
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<p>SEM images of nickel hydroxide generated under various conditions: (<b>a</b>) without agitation and (<b>b</b>) with agitation.</p>
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18 pages, 8024 KiB  
Article
Evaluating a Nickel–Metal Hydride (NiMH) Battery Regeneration Patent Based on a Non-Intrusive and Unsupervised Prototype
by Rafael Martínez-Sánchez, Angel Molina-García, Antonio Mateo-Aroca and Alfonso P. Ramallo-González
Batteries 2024, 10(11), 402; https://doi.org/10.3390/batteries10110402 - 14 Nov 2024
Viewed by 1342
Abstract
In the ongoing shift toward electric vehicles (EVs) primarily utilizing lithium-ion battery technology, a significant population of hybrid electric vehicles (HEVs) remains operational, which are reliant on established NiMH battery systems. Over the last twenty years, these HEVs have generated a substantial number [...] Read more.
In the ongoing shift toward electric vehicles (EVs) primarily utilizing lithium-ion battery technology, a significant population of hybrid electric vehicles (HEVs) remains operational, which are reliant on established NiMH battery systems. Over the last twenty years, these HEVs have generated a substantial number of NiMH batteries that are either inoperable, experiencing performance degradation, or approaching the end of their service life. This situation results in a twofold challenge: (i) a growing volume of environmentally hazardous waste due to the difficulty of NiMH battery reclamation and (ii) escalating maintenance costs for HEV owners necessitated by replacement battery purchases. To overcome this scenario, patent WO2015092107A1, published in 2015, proposed a ‘Method for regenerating NiMH batteries.’ This method claimed the ability to restore NiMH batteries to their original functionality based on a non-intrusive approach. However, a comprehensive review of the relevant scientific literature fails to identify any empirical evidence supporting the efficacy of this regeneration technique. Within this context, this study provides a detailed analysis and evaluation of the regeneration process based on an unsupervised and non-intrusive prototype. The proposed prototype can be used not only to implement and evaluate the previous patent, but also to test any other process or methodology based on controlled charging/discharging periods under certain current conditions. NiMH battery cells from a Toyota Prius were included in this work as a real case study. The experimental results from this prototype demonstrate the reduced potential for battery regeneration using the proposed method. Future contributions should offer a promising solution for mitigating the challenges associated with NiMH battery disposal, maintenance within the HEV domain, and other second-life alternative options. Full article
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<p>Operational scheme. General overview.</p>
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<p>General operation of the prototype.</p>
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<p>General electrical diagram of the prototype.</p>
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<p>Electrical diagram of the prototype in charging mode.</p>
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<p>Electrical diagram of the prototype in discharging mode.</p>
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<p>Power supplies for the cells and additional power supply for the process.</p>
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<p>Potentiometer for the discharging process (TE Connectivity, Type 23 Series).</p>
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<p>Display monitoring system (Caredy DT3010).</p>
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<p>Example of the selected relay (Elego ASDIOFJ1).</p>
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<p>Example of an A or B switch (RS PRO 1858229).</p>
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<p>Frontal panel. General overview.</p>
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<p>Rear panel with relays. Example.</p>
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<p>Energy charged in each cell. Data distribution for 9 process iterations.</p>
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<p>Energy discharged from each cell. Data distribution for 9 process iterations.</p>
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<p>Ratio of energy discharged and charged for each cell (in pu). Data distribution for 9 process iterations and statistical analysis.</p>
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<p>SOH in each cell for each process and statistical analysis.</p>
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<p>SOH of cell 21 in each process.</p>
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<p>SOH of cell 11 in each process.</p>
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<p>SOH of cell 3 in each process.</p>
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9 pages, 1759 KiB  
Article
Enhanced Cycling Stability of Amorphous MgNi-Based Alloy Electrodes through Corrosion Prevention by Incorporating Al2(SO4)3·18H2O into the Electrolyte
by Jiabao Li, Yang Cai, Jianling Huang, Shiqian Zhao and Deliang Cheng
Metals 2024, 14(10), 1142; https://doi.org/10.3390/met14101142 - 8 Oct 2024
Viewed by 855
Abstract
Mg-based alloy anodes suffer from severe corrosion in alkaline electrolytes, which substantially impedes their cycle life and thereby limits their suitability as anode materials for nickel–metal hydride (Ni-MH) batteries. This work modifies the conventional 6 M KOH electrolyte by adding 0.1 M Al [...] Read more.
Mg-based alloy anodes suffer from severe corrosion in alkaline electrolytes, which substantially impedes their cycle life and thereby limits their suitability as anode materials for nickel–metal hydride (Ni-MH) batteries. This work modifies the conventional 6 M KOH electrolyte by adding 0.1 M Al2(SO4)3·18H2O. The electrochemical hydrogen storage properties of Mg0.45Ti0.05Ni0.50 alloy in this electrolyte and its microstructural evolution during cycling are studied. In the 6 M KOH + 0.1 M Al2(SO4)3·18H2O electrolyte, a protective layer consisting of Mg2Al(OH)7 is formed on the surface of the Mg0.45Ti0.05Ni0.50 alloy anode during charge/discharge cycling instead of Mg(OH)2, effectively preventing further corrosion and improving its cycle life. The Mg0.45Ti0.05Ni0.50 alloy anode delivers a maximum discharge capacity of 479.0 mAh g−1 and maintains 318.4 mAh g−1 after 30 cycles in the 6 M KOH + 0.1 M Al2(SO4)3·18H2O electrolyte, which is significantly superior to that achieved in the 6 M KOH electrolyte (471.1 mAh g−1 and 201.8 mAh g−1, respectively). This work provides a new strategy for improving the cycle stability of Mg-based alloy anodes. Full article
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<p>The XRD patterns of the milled Mg<sub>0.45</sub>Ti<sub>0.05</sub>Ni<sub>0.50</sub> alloy.</p>
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<p>Charge/discharge curves (<b>a</b>) and cycle stability (<b>b</b>) of Mg<sub>0.45</sub>Ti<sub>0.05</sub>Ni<sub>0.50</sub> alloy electrode.</p>
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<p>XRD patterns of the Mg<sub>0.45</sub>Ti<sub>0.05</sub>Ni<sub>0.50</sub> alloy electrode after 15 (<b>a</b>) and 30 (<b>b</b>) cycles in 6 M KOH and 6 M KOH + 0.1 M Al<sub>2</sub>(SO<sub>4</sub>)<sub>3</sub>, and corresponding TG curves (<b>c</b>,<b>d</b>).</p>
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<p>Tafel curves of Mg<sub>0.45</sub>Ti<sub>0.05</sub>Ni<sub>0.50</sub> alloy electrode after 1 (<b>a</b>), 15 (<b>b</b>), and 30 (<b>c</b>) cycles in 6 M KOH and 6 M KOH + 0.1 M Al<sub>2</sub>(SO<sub>4</sub>)<sub>3</sub>·18H<sub>2</sub>O, and corresponding corrosion potential (<b>d</b>).</p>
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15 pages, 7598 KiB  
Article
Processing and Characterization of Spent Nickel–Metal Hydride Type AA Batteries to Recover Valuable Materials (Cobalt, Nickel and Rare Earth Elements)
by Gheorghe Iacob, Valeriu-Gabriel Ghica, Florentina Niculescu, Mircea-Ionuţ Petrescu and Ana Vasile
Materials 2024, 17(19), 4908; https://doi.org/10.3390/ma17194908 - 7 Oct 2024
Viewed by 1076
Abstract
The experimental research was focused on the investigation of valuable material from spent Ni-MH type AA batteries, namely the metal grid anodes and the black mass material (anode and cathode powder). The materials of interest were analyzed by X-ray fluorescence spectroscopy (XRF), ICP-OES [...] Read more.
The experimental research was focused on the investigation of valuable material from spent Ni-MH type AA batteries, namely the metal grid anodes and the black mass material (anode and cathode powder). The materials of interest were analyzed by X-ray fluorescence spectroscopy (XRF), ICP-OES (inductively coupled plasma optical emission spectrometry), optical microscopy, scanning electron microscopy (SEM), energy-dispersive X-ray analysis (EDX), electron backscatter diffraction (EBSD), and X-ray diffraction (XRD). The analyzed grids have a high Fe content, but some of them correspond to the Invar alloy with approx. 40% Ni. In the black mass material, round particles and large aggregations were observed by SEM analysis, showing a high degree of degradation. The XRD analysis reveals the presence of only three compounds or phases that crystallize in the hexagonal system: La0.52Ce0.33Pr0.04Nd0.11Co0.6Ni4.4, Ni(OH)2, and La5Ni19. The obtained results provide useful and interesting information that can be used for further research in the recycling and economic assessment of metals from spent Ni-MH batteries. Full article
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<p>Processing of Ni-MH batteries: (<b>a</b>) before dismantling, (<b>b</b>) after dismantling, (<b>c</b>) crushing the mixed material, (<b>d</b>) washing with distilled water, (<b>e</b>,<b>f</b>) the filtration process, (<b>g</b>) oven drying the powder, (<b>h</b>) metallic casings, (<b>i</b>) grids, (<b>j</b>) non-metallic fraction after drying, (<b>k</b>) powder after oven drying, (<b>l</b>,<b>m</b>) sieving, (<b>n</b>) the coarse product obtained after sieving (mixture of pieces of metal grids with mixed content and non-metallic fraction), (<b>o</b>) magnetic separation, (<b>p</b>) pieces of magnetically extracted metal grids, (<b>q</b>) final powder.</p>
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<p>Images of the metal grids found in processed Ni-MH batteries: (<b>a</b>) type 1 (T1), (<b>b</b>) type 2 (T2) and (<b>c</b>) type 3 (T3).</p>
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<p>Optical microscopy images of metal grids: (<b>a</b>) anode grid (T1); (<b>b</b>) anode grid (T1); (<b>c</b>–<b>f</b>) anode grid (T3).</p>
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<p>Representative SEM images of black mass material (anodic and cathodic powder).</p>
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<p>EDX1 spectrum associated with <a href="#materials-17-04908-f004" class="html-fig">Figure 4</a>.</p>
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<p>EDX2 spectrum associated with <a href="#materials-17-04908-f004" class="html-fig">Figure 4</a>.</p>
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<p>EDX3 spectrum associated with <a href="#materials-17-04908-f004" class="html-fig">Figure 4</a>.</p>
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<p>EBSD mapping and EDS analysis for the black mass material showing the distribution of elements O, La, Ce, Pr, Nd, Co, Ni and Ta in the respective area.</p>
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<p>The diffractogram of the black mass material.</p>
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21 pages, 3233 KiB  
Article
Sensor Fusion-Based Pulsed Controller for Low Power Solar-Charged Batteries with Experimental Tests: NiMH Battery as a Case Study
by Shyam Yadasu, Vinay Kumar Awaar, Vatsala Rani Jetti and Mohsen Eskandari
Batteries 2024, 10(9), 335; https://doi.org/10.3390/batteries10090335 - 21 Sep 2024
Cited by 1 | Viewed by 939
Abstract
Solar energy is considered the major source of clean and ubiquitous renewable energy available on various scales in electric grids. In addition, solar energy is harnessed in various electronic devices to charge the batteries and power electronic equipment. Due to its ubiquitous nature, [...] Read more.
Solar energy is considered the major source of clean and ubiquitous renewable energy available on various scales in electric grids. In addition, solar energy is harnessed in various electronic devices to charge the batteries and power electronic equipment. Due to its ubiquitous nature, the corresponding market for solar-charged small-scale batteries is growing fast. The most important part to make the technology feasible is a portable battery charger and the associated controllers to automate battery charging. The charger should consider the case of charging to be convenient for the user and minimize battery degradation. However, the issue of slow charging and premature battery life loss plagues current industry standards or innovative battery technologies. In this paper, a new pulse charging technique is proposed that obviates battery deterioration and minimizes the overall charging loss. The solar-powered battery charger is prototyped and executed as a practical, versatile, and compact photovoltaic charge controller at cut rates. With the aid of sensor fusion, the charge controller is disconnected and reconnects the battery during battery overcharging and deep discharging conditions using sensors with relays. The laboratory model is tested using a less expensive PV panel, battery, and digital signal processor (DSP) controller. The charging behavior of the solar-powered PWM charge controller is studied compared with that of the constant voltage–constant current (CV–CC) method. The proposed method is pertinent for minimizing energy issues in impoverished places at a reasonable price. Full article
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<p>Schematic illustration of the proposed charge controller.</p>
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<p>Equivalent circuit diagram.</p>
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<p>The PV cell model.</p>
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<p>Illustration of DC-DC converter equivalent circuit.</p>
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<p>Illustration of the proposed method functional blocks.</p>
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<p>PID controller block diagram.</p>
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<p>Experimental setup for determining the impact of charge algorithms on battery.</p>
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<p>Origalysis electrochemical workstation.</p>
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<p>Input Voltage.</p>
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<p>Standard protocol with an equal duty cycle.</p>
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<p>Output high-frequency Pulse Current.</p>
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<p>Charge–discharge studies of NiMH batteries using conventional methods with respect to voltages: (<b>a</b>) Total charge time; (<b>b</b>) Total discharge time; (<b>c</b>) Total discharge capacity.</p>
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<p>Charge–discharge studies of NiMH batteries using pulse methods with respect to voltages: (<b>a</b>) Total charge time; (<b>b</b>) Total discharge time; (<b>c</b>) Total discharge capacity.</p>
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<p>A Nyquist graph of an EIS study with NiMH battery: (<b>a</b>) Battery impedance before charging; (<b>b</b>) Impedance with conventional charging; (<b>c</b>) Impedance with pulse charging.</p>
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<p>Thermal analysis of NiMH battery: (<b>a</b>) Temperature measurements using sensor probe; (<b>b</b>) Temperature variations in CCCV and Pulse charging methods (t<sub>c</sub> &amp; t<sub>p</sub>).</p>
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18 pages, 6032 KiB  
Article
Evaluating a Fe-Based Metallic Glass Powder as a Novel Negative Electrode Material for Applications in Ni-MH Batteries
by Oscar Sotelo, John Henao, Carlos Poblano, Bernardo Campillo, Erick Castañeda, Néstor Flores, Arturo Molina and Horacio Martínez
Batteries 2024, 10(9), 312; https://doi.org/10.3390/batteries10090312 - 1 Sep 2024
Viewed by 1215
Abstract
Metallic glasses (MGs) are a type of multicomponent non-crystalline metallic alloys obtained by rapid cooling, which possess several physical, mechanical, and chemical advantages against their crystalline counterparts. In this work, an Fe-based MG is explored as a hydrogen storage material, especially, due to [...] Read more.
Metallic glasses (MGs) are a type of multicomponent non-crystalline metallic alloys obtained by rapid cooling, which possess several physical, mechanical, and chemical advantages against their crystalline counterparts. In this work, an Fe-based MG is explored as a hydrogen storage material, especially, due to the evidence in previous studies about the capability of some amorphous metals to store hydrogen. The evaluation of an Fe-based MG as a novel negative electrode material for nickel/metal hydride (Ni-MH) batteries was carried out through cyclic voltammetry and galvanostatic charge–discharge tests. A conventional LaNi5 electrode was also evaluated for comparative purposes. The electrochemical results obtained by cyclic voltammetry showed the formation of three peaks, which are associated with the formation of Fe oxides/oxyhydroxides and hydroxides. Cycling charge/discharge tests revealed activation of the MG electrode. The highest discharge capacity value was 173.88 mAh/g, but a decay in its capacity was observed after 25 cycles, contrary to the LaNi5, which presents an increment of the discharge capacity for all the current density values evaluated, reached its value maximum at 183 mAh/g. Characterization analyses performed by X-ray diffraction, Scanning Electron Microscopy and Raman Spectroscopy revealed the presence of corrosion products and porosity on the surface of the Fe-based MG electrodes. Overall, the Fe-based MG composition is potentially able to work as a negative electrode material, but degradation and little information about storage mechanisms means that it requires further investigation. Full article
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<p>SEM and XRD analysis of powder of Fe-based metallic glass (<b>a</b>,<b>b</b>) and LaNi<sub>5</sub> (<b>c</b>,<b>d</b>) as feedstock powder.</p>
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<p>Cyclic voltammogram of the Fe-based MG negative electrode in KOH 6M at room temperature.</p>
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<p>Cyclic voltammogram of the LaNi<sub>5</sub> negative electrode in KOH 6M at room temperature.</p>
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<p>Discharge capacity vs. cycle number for the Fe-based MG electrode (<b>a</b>) and LaNi<sub>5</sub> electrode (<b>b</b>). These curves were obtained at current density values of 50, 100 and 125 mA/g in KOH 6M.</p>
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<p>Coulombic efficiency vs. cycle number for the Fe-based MG electrode at current density values of 50, 100 and 125 mA/g.</p>
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<p>Nyquist plot obtained from the EIS technique at 0, 5 and 10 charge–discharge cycles.</p>
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<p>XRD analysis after electrochemical evaluation by cyclic voltammetry in a potential range of −1.2 V to −0.2 V.</p>
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<p>Raman analysis of the Fe-based MG as received, and Fe-based MG tested after cyclic voltammetry in a potential range of −1.2 V to −0.2 V.</p>
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<p>SEM analysis of Fe-based MG negative electrode (cold-pressed) before (<b>a</b>) and after (<b>b</b>) cyclic voltammetry tests.</p>
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<p>Element mapping analysis of Fe-based MG particles after electrochemical evaluation by cyclic voltammetry.</p>
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16 pages, 2808 KiB  
Article
Designing a Twin Frequency Control DC-DC Buck Converter Using Accurate Load Current Sensing Technique
by Chiang Liang Kok and Liter Siek
Electronics 2024, 13(1), 45; https://doi.org/10.3390/electronics13010045 - 20 Dec 2023
Cited by 6 | Viewed by 1332
Abstract
In this paper, a buck DC-DC converter with the proposed twin frequency control scheme (TFCS) and accurate load current sensing (ALCS) was designed and implemented with 0.18 µm CMOS technology for a supply voltage ranging from 2.0 to 3.0 V, which is compatible [...] Read more.
In this paper, a buck DC-DC converter with the proposed twin frequency control scheme (TFCS) and accurate load current sensing (ALCS) was designed and implemented with 0.18 µm CMOS technology for a supply voltage ranging from 2.0 to 3.0 V, which is compatible with state-of-the-art batteries (NiCd/NiMH: 1.1–2 V, Li-Ion: 2.5–4.2 V). The proposed converter yields a peak efficiency of about 92.7% with a load current of 30 mA. Furthermore, it only occupies a silicon area of 1.3 mm2. The proposed buck converter is dedicated for smartphone applications whereby it spends most of its time in idle, low load conditions. Full article
(This article belongs to the Special Issue Advances in SoCs and Embedded Systems)
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<p>A vital part of the 3G/4G smartphone power management unit (PMU).</p>
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<p>Proposed twin frequency control DC-DC buck converter using accurate load current sensing technique.</p>
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<p>Accurate load current sensing (ALCS) block.</p>
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<p>Four-bit thermometer code ADC.</p>
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<p>Proposed twin frequency control scheme (TFCS).</p>
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<p>Optimized sizing of (<b>a</b>) NMOS power transistor; (<b>b</b>) PMOS power transistor.</p>
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<p>Die photo of the buck converter with proposed TFCS and ALCS.</p>
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<p>Prototype of a buck converter with proposed TFCS and ALCS.</p>
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<p>Peak efficiency achieved—waveform of <span class="html-italic">V<sub>x</sub></span> and <span class="html-italic">V</span><sub>int</sub> (<span class="html-italic">V<sub>BATT</sub></span> = 2 V, <span class="html-italic">V<sub>out</sub></span> = 1.25 V, Freq = 250 kHz and <span class="html-italic">I<sub>load</sub></span> = 30 mA).</p>
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<p>Power efficiency of the proposed TFCS and ALCS buck converter and the conventional PWM/PFM controller under different loading conditions (P—Proposed Work; C—Conventional Work).</p>
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<p>Efficiency improvement of the proposed TFCS and ALCS buck converter compared to the latest state-of-the-art work [<a href="#B28-electronics-13-00045" class="html-bibr">28</a>].</p>
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24 pages, 5636 KiB  
Article
Selective Precipitation of Rare Earth Double Sulfate Salts from Industrial Ni–MH Battery Leachates: Impact of Downstream Processing on Product Quality
by Boris Guzhov, Laurent Cassayre, Antoine Barnabé, Nicolas Coppey and Béatrice Biscans
Batteries 2023, 9(12), 574; https://doi.org/10.3390/batteries9120574 - 28 Nov 2023
Cited by 2 | Viewed by 2827
Abstract
This work focuses on the recovery of rare earth elements (REEs = La, Ce, Nd, Pr) from spent nickel–metal hydride batteries by hydrometallurgical processing. The REEs were precipitated in the form of sodium-lanthanide double sulfate salts by adding Na2SO4 to [...] Read more.
This work focuses on the recovery of rare earth elements (REEs = La, Ce, Nd, Pr) from spent nickel–metal hydride batteries by hydrometallurgical processing. The REEs were precipitated in the form of sodium-lanthanide double sulfate salts by adding Na2SO4 to a leach liquor prepared from industrially processed spent batteries. The objectives were to better understand the parameters driving the purity of the product and to identify the phases involved, as well as their crystallographic structure. The methodology included experiments performed in a 2 L reactor, thermodynamic calculations and product characterization. We confirmed that high REE precipitation yields (>95%) can be achieved under a wide range of hydrodynamic conditions. Furthermore, we demonstrated and quantified how appropriately washing the product allows for a significant reduction in nickel losses while maintaining control over REE product purity. Finally, using X-ray Diffraction analyses, it was established that REEs form a solid solution with a chemical formula (Na0.9K0.1)(La0.65Ce0.24Pr0.04Nd0.07)(SO4)2·H2O, which has not been reported so far. Full article
(This article belongs to the Section Battery Processing, Manufacturing and Recycling)
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<p>Precipitation/washing/drying protocol for the study of REE double sulfate production from spent Ni–MH battery leachate.</p>
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<p>Solubility of La (<b>a</b>) and Ce (<b>b</b>) salts (g of REE/L of solution) in H<sub>2</sub>SO<sub>4</sub>–H<sub>2</sub>O media at 25 °C (calculated with OLI–MSE [<a href="#B35-batteries-09-00574" class="html-bibr">35</a>]; experimental data for Na, K–La, Ce double sulfate salts from Lokshin et al. [<a href="#B40-batteries-09-00574" class="html-bibr">40</a>]).</p>
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<p>Rates of metal elements in solution calculated at thermodynamic equilibria as a function of the addition of 2.87 mol/L Na<sub>2</sub>SO<sub>4</sub> solution in the industrial PLS at 60 °C.</p>
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<p>Evolution of the REE concentrations in the aqueous phase with time during the addition of 2.87 mol/L Na<sub>2</sub>SO<sub>4</sub> solution at 60 °C and ripening time for 1 h.</p>
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<p>(<b>a</b>) Comparison of experimental and calculated yields of precipitation of rare earth elements after standard precipitation experiment (60 °C, 7 g/min of 2.87 mol/L Na<sub>2</sub>SO<sub>4</sub>, Na:REE = 3.6:1, 550 rpm, 1 h of ripening) and (<b>b</b>) comparison between calculated and experimental amount of REEs in solution as a function of the Na:REE molar ratio (with exp. data from [<a href="#B31-batteries-09-00574" class="html-bibr">31</a>,<a href="#B35-batteries-09-00574" class="html-bibr">35</a>]).</p>
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<p>Influence of hydrodynamic parameters on the precipitation reaction of REEs (<b>a</b>) stirring rate (T = 60 °C; Na:REE = 3.6:1; Na<sub>2</sub>SO<sub>4</sub> = 7 g/min) and (<b>b</b>) Na<sub>2</sub>SO<sub>4</sub> flow rate (T = 60 °C; Na:REE = 3.6:1; 550 rpm).</p>
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<p>Concentrations (g/L) of (<b>a</b>) Ni and (<b>b</b>) REEs in filtrates during filtration-washing steps. (<b>c</b>) Ce:La and Nd:La ratios (g/g) in the filtrates. (<b>d</b>) Comparison of Ni and REE concentrations in the filtrates during washing by 2.5 L of H<sub>2</sub>O.</p>
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<p>SEM images of Na–REE double sulfates salts. (<b>a</b>) Sample before washing and (<b>b</b>) sample after washing at RT.</p>
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<p>SEM–EDS elemental mapping of (<b>a</b>) non-washed and (<b>b</b>) washed Na–REE double sulfate salts (EDS spectra are outlined in the <a href="#app1-batteries-09-00574" class="html-app">supplementary materials</a>). (<b>c</b>) Corresponding XRD patterns with the non-washed sample in black and with the washed sample in grey. Bragg’s peak of the trigonal NaREE(SO<sub>4</sub>)<sub>2</sub>·H<sub>2</sub>O and NiSO<sub>4</sub>·H<sub>2</sub>O are represented in blue and green, respectively.</p>
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<p>Recommended protocol for washing of the REEs-rich filter cake.</p>
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<p>TGA curves of 3 samples (blue, red and black lines) of washed Na–REE double sulfate salts (N<sub>2</sub>, 10 °C/min, isothermal at 105 °C and 500 °C for 15 min).</p>
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<p>(<b>a</b>) The XRD patterns of the synthetic NaLa(SO<sub>4</sub>)<sub>2</sub>·H<sub>2</sub>O, NaCe(SO<sub>4</sub>)<sub>2</sub>·H<sub>2</sub>O and the mixed compound NaLa<sub>0</sub><sub>.</sub><sub>5</sub>Ce<sub>0</sub><sub>.</sub><sub>5</sub>(SO<sub>4</sub>)<sub>2</sub>·H<sub>2</sub>O. (<b>b</b>) Output from the profile matching refinement analysis of the XRD pattern for the washed product obtained from the industrial PLS. (<b>c</b>) Variation of REE double sulfate unit cell with ionic radius of the corresponding REE.</p>
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14 pages, 10377 KiB  
Article
Load Capacity of Nickel–Metal Hydride Battery and Proton-Exchange-Membrane Fuel Cells in the Fuel-Cell-Hybrid-Electric-Vehicle Powertrain
by Ireneusz Pielecha, Filip Szwajca and Kinga Skobiej
Energies 2023, 16(22), 7657; https://doi.org/10.3390/en16227657 - 19 Nov 2023
Cited by 1 | Viewed by 1240
Abstract
This article investigates the impact of loading on the hybrid powertrain of the FCAT-30 model, equipped with a proton-exchange-membrane fuel cell (PEMFC) and a nickel–metal hydride (NiMH) battery. This study involves analyzing structural component performance based on voltage and current measurements of the [...] Read more.
This article investigates the impact of loading on the hybrid powertrain of the FCAT-30 model, equipped with a proton-exchange-membrane fuel cell (PEMFC) and a nickel–metal hydride (NiMH) battery. This study involves analyzing structural component performance based on voltage and current measurements of the fuel cell, battery, and powertrain. Tests conducted under different load conditions reveal significant differences in battery current and fuel-cell voltage, highlighting the crucial role of the battery in the powertrain. External loading induces cyclic operation of the fuel cell, generating peak power. The energy balance analysis demonstrates that, under no-load conditions, the vehicle consumes 37.3% of its energy from the fuel cell, with a total energy consumption of 3597 J. Under load, the energy from the battery is significantly utilized, resulting in a constant fuel-cell share of approximately 19%, regardless of the vehicle’s load. This study concludes that the battery predominantly drives the powertrain, with the fuel cell acting as a secondary energy source. These findings provide valuable insights into the power distribution and energy balance in the hybrid powertrain. Using a load driving profile reduced the fuel-cell-stack energy contribution by 6.85% relative to driving without an external load. Full article
(This article belongs to the Special Issue Battery Modelling, Applications, and Technology)
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<p>FCAT30 hydrogen model of hybrid powertrain with NiMH battery (photo owner).</p>
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<p>Diagram of energy flow in a hybrid drive system.</p>
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<p>A view of the components of the hybrid propulsion system, including the data acquisition and visualization system.</p>
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<p>View of the chassis dynamometer with its most important components.</p>
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<p>View of the chassis dynamometer software screen.</p>
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<p>Vehicle speed profiles on the chassis dynamometer: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Test results of measured quantities during hybrid drive tests: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Magnitudes of cell and battery power during speed profile analysis: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Changes in voltage and current of the cell under operating conditions: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Voltage–current characteristics of the fuel cell: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Voltage–current characteristics of the battery: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Power shares of hybrid drive system components under operating conditions: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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<p>Changes in energy of the battery and fuel cell under operating conditions: (<b>a</b>) without load and (<b>b</b>) with load.</p>
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31 pages, 20172 KiB  
Article
Electric Vehicle NiMH Battery State of Charge Estimation Using Artificial Neural Networks of Backpropagation and Radial Basis
by Jordy Alexander Hernández, Efrén Fernández and Hugo Torres
World Electr. Veh. J. 2023, 14(11), 312; https://doi.org/10.3390/wevj14110312 - 17 Nov 2023
Cited by 3 | Viewed by 2856
Abstract
The state of charge of a battery depends on many magnitudes, but only voltage and intensity are included in mathematical equations because other variables are complex to integrate into. The contribution of this work was to obtain a model to determine the state [...] Read more.
The state of charge of a battery depends on many magnitudes, but only voltage and intensity are included in mathematical equations because other variables are complex to integrate into. The contribution of this work was to obtain a model to determine the state of charge with these complex variables. This method was developed considering four models, the multilayer feed-forward backpropagation models of two and three input variables used supervised training, with the variable-learning-rate backpropagation training function, five and seven neurons in the hidden layer, respectively, achieving an optimal training. Meanwhile, the radial basis neural network models of two and three input variables were trained with the hybrid method, the propagation constant with a value of 1 and 80 neurons in the hidden layer. As a result, the radial basis neural network with the variable-learning-rate training function, considering the discharge temperature, was the one with the best performance, with a correlation coefficient of 0.99182 and a confidence interval of 95% (0.98849; 0.99516). It is then concluded that artificial neural networks have high performance when modeling nonlinear systems, whose parameters are difficult to measure with time variation, so estimating them in formulas where they are omitted is no longer necessary, which means an accurate SOC. Full article
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<p>Methods for performance analysis.</p>
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<p>RC circuit used to develop the model.</p>
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<p>Inputs and outputs of the artificial neural network of the first model.</p>
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<p>Inputs and outputs of the artificial neural network of the second model.</p>
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<p>Test station for data acquisition.</p>
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<p>Voltage and temperature in the discharge process.</p>
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<p>Current and temperature in the discharge process.</p>
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<p>Structure of the feed-forward backpropagation neural network of the second method with 2 layers.</p>
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<p>Feed-forward backpropagation training phase.</p>
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<p>Radial basis hybrid training phase.</p>
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<p>Standard neural structure.</p>
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<p>Best validation performance in terms of MSE.</p>
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<p>Training state plot comprises gradient, scalar μ, and validation check.</p>
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<p>Difference between the actual and the target output.</p>
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<p>Regression relation of the FBNN network.</p>
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<p>Feed-forward in a three-layer network. The superscripts represent the layer number.</p>
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<p>Regression relation of the RBNN network.</p>
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<p>FBNN and RBNN results with temperature.</p>
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<p>FBNN and RBNN results without temperature.</p>
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<p>Performance comparison of the developed methods.</p>
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<p>SOC comparisons of different FBNN configurations with temperature.</p>
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<p>SOC comparisons of different FBNN configurations without temperature.</p>
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<p>SOC interval graph of the different models developed, 95% confidence interval of the mean.</p>
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<p>Difference of the means for the different methods.</p>
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14 pages, 19859 KiB  
Article
Chemical Structure Comparison via Scanning Electron Microscopy of Spent Commercial Nickel–Metal Hydride Batteries
by Thomas Walther
Materials 2023, 16(17), 5761; https://doi.org/10.3390/ma16175761 - 23 Aug 2023
Viewed by 1657
Abstract
Back-scattered electron imaging and X-ray elemental mapping were combined in a tabletop scanning electron microscope (SEM) to investigate cross-sections of three AA-type (mignon) nickel–metal hydride (NiMH) batteries from different manufacturers. All batteries underwent 500–800 charge/discharge cycles and reached their end of lifetime after [...] Read more.
Back-scattered electron imaging and X-ray elemental mapping were combined in a tabletop scanning electron microscope (SEM) to investigate cross-sections of three AA-type (mignon) nickel–metal hydride (NiMH) batteries from different manufacturers. All batteries underwent 500–800 charge/discharge cycles and reached their end of lifetime after several years as they could no longer hold any significant electric charge (less than 20% of nominal charge capacity), but none showed any short-circuiting. The types of degradation observed in this field study included electrode swelling, metallic nickel formation and carbon incorporation into pores in the positive electrodes and, in the negative electrodes, metal alloy segregation of different elements such as nickel, lanthanum and, in one case, sodium, as well as grain break-up and pore formation. All these phenomena could readily be observed at rather small magnifications. This will be important for the improvement of NiMH batteries, for which new generations with nominally slightly increased charge capacities are being marketed all the time. Full article
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<p>SE (<b>a</b>–<b>c</b>, top row) and BSE images (<b>d</b>–<b>f</b>, bottom row) of cross-sections of all three samples at low magnification of 30×. Horizontal field of view (hFoV): 5.6 mm. From left to right: (<b>a</b>,<b>d</b>) sample A, (<b>b</b>,<b>e</b>) sample B and (<b>c</b>,<b>f</b>) sample C.</p>
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<p>BSE images of cross-sections of outermost regions of cross-sections from samples B (<b>a</b>) and C (<b>b</b>) and at medium magnification of 100×. hFoV: 1.7 mm.</p>
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<p>EDX spectra from the three sample areas shown in <a href="#materials-16-05761-f001" class="html-fig">Figure 1</a>d–f. Elements with labels above the peaks have been used for X-ray mapping in Figures 4 and 6, those with labels below are omitted because they showed only noise.</p>
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<p>EDX maps of the major constituents from the same regions of each sample, including carbon, oxygen and the metals iron, cobalt and nickel. (<b>a</b>–<b>o</b>) Each element is shown in a different color in the rows; each column refers to a different sample. More maps from the same regions are shown in Figure 6. hFoV: 5.6 mm.</p>
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<p>Representative composite EDX maps of cross-sections from samples B (<b>a</b>) and C (<b>b</b>) at higher magnification of 120×. hFopV: 1.4 mm. red: O, green: Ni, blue: Fe. Arrows indicate beginning dendrite growth into the separator.</p>
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<p>(<b>a</b>–<b>w</b>) EDX maps of less abundant elements from the same regions as shown in <a href="#materials-16-05761-f004" class="html-fig">Figure 4</a>. Maps that showed only noise, e.g., distribution of alkaline metals for samples A and B, have been omitted for clarity.</p>
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<p>(<b>a</b>–<b>w</b>) EDX maps of less abundant elements from the same regions as shown in <a href="#materials-16-05761-f004" class="html-fig">Figure 4</a>. Maps that showed only noise, e.g., distribution of alkaline metals for samples A and B, have been omitted for clarity.</p>
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19 pages, 5006 KiB  
Article
Investigation on the Effect of Mesomixing on Crystal Quality during Antisolvent Crystallization of Nd2(SO4)3·8H2O
by Tinjombo Octavious Baloyi, Jemitias Chivavava and Alison Emslie Lewis
Metals 2023, 13(8), 1378; https://doi.org/10.3390/met13081378 - 31 Jul 2023
Viewed by 1162
Abstract
Rare earth elements (REEs) are essential for permanent magnets that are vital for wind turbines and electric vehicles motors (EV), and are also used in a range of high-tech devices such as smartphones, digital cameras, and electronic displays. Nickel metal hydride (NiMH) batteries [...] Read more.
Rare earth elements (REEs) are essential for permanent magnets that are vital for wind turbines and electric vehicles motors (EV), and are also used in a range of high-tech devices such as smartphones, digital cameras, and electronic displays. Nickel metal hydride (NiMH) batteries have been identified as a potential source due to their short lifespans and an anticipated boom in the production of EV. The aim of this study was to investigate the effect of mesomixing on crystal quality in a non-confined impinging jet mixer (NCIJM) during antisolvent crystallization of 3.2 g/L Nd2(SO4)3 from a synthetic leach solution of NiMH battery using ethanol at an O/A ratio of 1.1. The jet streams were supplied at a Reynolds number (Re) between 7500 and 15,000. The product slurry was allowed to further crystallize in a stirred batch crystallizer at a Re of 13,000 for 45 s. An average yield of 90% was achieved. Laser diffraction and scanning electron microscopy (SEM) were used for size analysis. The initial results were inconclusive due to the secondary mixing effect in the stirred batch crystallizer. Therefore, the experiments were repeated, and samples were collected immediately after mixing in the NCIJM onto a porous grid placed on a high absorbance filter paper to abruptly halt crystallization. The samples were analysed using a transmission electron microscope (TEM), and the acquired images were processed using ImageJ to obtain crystal size distributions (CSDs). It was found that the enhanced mesomixing conditions resulted in smaller crystal sizes and narrower CSDs. This was because the nucleation rate was found to be mass-transfer-limited, such that higher mesomixing intensities promoted the nucleation rate from 6 × 1012 to 5 × 1013 m−3 s−1 and, therefore, favoured the formation of smaller crystals. In parallel, intensified mesomixing resulted in uniform distribution of the supersaturation and, hence, narrowed the CSDs. Full article
(This article belongs to the Section Extractive Metallurgy)
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<p>Intensified mixing in the NCIJM.</p>
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<p>Solubility and yield curves modelled from OLI Stream Analyzer [<a href="#B17-metals-13-01378" class="html-bibr">17</a>] at 23 °C and atmospheric pressure.</p>
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<p>Particle size distribution as a function of intensified mesomixing in the NCIJM.</p>
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<p>Mean, median, and modal crystal sizes, as well as span as a function of mesomixing intensity in the NCIJM.</p>
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<p>Images showing particles crystallized in a NCIJM at <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>m</mi> <mi>e</mi> <mi>s</mi> <mi>o</mi> </mrow> </msub> </mrow> </semantics></math> of (<b>A</b>) −470, (<b>B</b>) −390, (<b>C</b>) −340, and (<b>D</b>) −300 μs, after which the suspension was allowed to age in a stirred batch crystallizer for 45 s.</p>
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<p>Product yields obtained at different mesomixing intensities.</p>
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<p>Images showing an increase in a number of crystals and a reduction in crystal sizes as <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>m</mi> <mi>e</mi> <mi>s</mi> <mi>o</mi> </mrow> </msub> </mrow> </semantics></math> was reduced. The corresponding <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>m</mi> <mi>e</mi> <mi>s</mi> <mi>o</mi> </mrow> </msub> </mrow> </semantics></math> values were as follows: (<b>A</b>) −470, (<b>B</b>) −390, (<b>C</b>) −340, and (<b>D</b>) −300 µs.</p>
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<p>Crystal size distribution as a function of <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>m</mi> <mi>e</mi> <mi>s</mi> <mi>o</mi> </mrow> </msub> </mrow> </semantics></math>.</p>
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<p>Mean, modal, and median crystal sizes, as well as span as a function of the mesomixing time constant.</p>
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<p>Random SEM and TEM images showing (<b>A</b>) particles stacked on top of each other; (<b>B</b>) breakage; and (<b>C</b>,<b>D</b>) single crystals.</p>
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<p>Effect of <math display="inline"><semantics> <mrow> <msub> <mrow> <mi>τ</mi> </mrow> <mrow> <mi>m</mi> <mi>i</mi> <mi>c</mi> <mi>r</mi> <mi>o</mi> </mrow> </msub> </mrow> </semantics></math> on nucleation rate and induction time.</p>
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32 pages, 13027 KiB  
Review
Surface Modifications of Magnesium-Based Materials for Hydrogen Storage and Nickel–Metal Hydride Batteries: A Review
by Yinglong Kang, Kemin Zhang and Xi Lin
Coatings 2023, 13(6), 1100; https://doi.org/10.3390/coatings13061100 - 14 Jun 2023
Cited by 7 | Viewed by 2930
Abstract
Whether it is fossil energy or renewable energy, the storage, efficient use, and multi-application of energy largely depend on the research and preparation of high-performance materials. The research and development of energy storage materials with a high capacity, long cycle life, high safety, [...] Read more.
Whether it is fossil energy or renewable energy, the storage, efficient use, and multi-application of energy largely depend on the research and preparation of high-performance materials. The research and development of energy storage materials with a high capacity, long cycle life, high safety, and high cleanability will improve the properties of energy storage systems and promote their wide application. In recent years, Mg-based materials, from a comprehensive consideration of energy storage performance, raw material reserves, and prices, have demonstrated potential industrial applications as large-scale hydrogen storage materials. Nevertheless, Mg-based materials also have obvious disadvantages: as a hydrogen storage material, the hydrogen absorption/desorption rate is insufficient, as well as the high hydrogen absorption/desorption temperatures; as the electrode material of Ni-MH batteries, the reactions of Mg with alkaline electrolyte and corrosion are the main problems for applications. This article reviews different surface treatment methods and mechanisms for surface modifications of Mg-based materials for hydrogen storage and Ni-MH battery applications, as well as the performance of the materials after surface modifications. Multiple experimental studies have shown that the surface layer or state of Mg-based materials has a strong impact on their performance. Surface modification treatment can greatly improve the energy storage performance of magnesium-based materials for hydrogen storage and Ni-MH battery applications. Specifically, Mg-based materials can have a lower hydrogen absorption/desorption temperature and a faster hydrogen absorption/desorption rate when used as hydrogen storage materials and can improve the corrosion resistance, initial discharge capacity, and cycling stability in alkaline solutions when used as negative electrode materials for Ni-MH batteries. By offering an overview of the surface modification methods for Mg-based materials in two energy storage fields, this article can improve researchers’ understanding of the surface modification mechanism of Mg-based materials and contribute to improving material properties in a more targeted manner. While improving the material properties, the material’s preparation and surface modification treatment process are considered comprehensively to promote the development, production, and application of high-performance Mg-based materials. Full article
(This article belongs to the Special Issue Surface Function Enhancement of Energy Storage Materials)
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<p>Schematic illustration of the hydrogen absorption process of Mg.</p>
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<p>Schematic illustration of MgH<sub>2</sub>/Co@CNT and its synergetic catalytic effect. Reprinted with permission from Ref. [<a href="#B62-coatings-13-01100" class="html-bibr">62</a>]. Copyright 2019, Elsevier.</p>
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<p>Schematic representation of catalytic mechanism of Fe<sub>3</sub>O<sub>4</sub>@GS on MgH<sub>2</sub>/Mg. Reprinted with permission from Ref. [<a href="#B64-coatings-13-01100" class="html-bibr">64</a>]. Copyright 2016, Royal Society of Chemistry.</p>
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<p>Schematic illustration of the catalytic mechanism of Ni, Mg<sub>2</sub>Ni, MgS, and rGO during the hydrogen absorption/desorption processes of the Mg-NiS/rGO nanocomposite. Reprinted with permission from Ref. [<a href="#B65-coatings-13-01100" class="html-bibr">65</a>]. Copyright 2017, Elsevier.</p>
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<p>Effect of size on the total energy of MgH<sub>2</sub> nanoparticles. Reprinted with permission from Ref. [<a href="#B92-coatings-13-01100" class="html-bibr">92</a>]. Copyright 2012, American Chemical Society.</p>
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<p>Changes in Δ<span class="html-italic">H</span> and Δ<span class="html-italic">S</span> caused by the size of Mg nanoparticles. Reprinted with permission from Ref. [<a href="#B93-coatings-13-01100" class="html-bibr">93</a>]. Copyright 2014, Royal Society of Chemistry.</p>
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<p>Many interfaces exist between MgH<sub>2</sub>, high and low valent Ti compounds during hydrogen desorption of Ti−based multivalence catalyst−doped MgH<sub>2</sub> system (<b>a</b>), the multivalent Ti acts as an intermediate medium for electron transfer (<b>b</b>), the catalytic mechanism of multivalent Ti (<b>c</b>). Reprinted with permission from Ref. [<a href="#B96-coatings-13-01100" class="html-bibr">96</a>]. Copyright 2013, Royal Society of Chemistry.</p>
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<p>A section schematic of Mg−TM (<b>a</b>) and ball-milled Mg−TM−based catalyst (<b>b</b>). Reprinted with permission from Ref. [<a href="#B97-coatings-13-01100" class="html-bibr">97</a>]. Copyright 2014, Royal Society of Chemistry.</p>
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<p>TPD-MS test curves of Mg−TM sample. Reprinted with permission from Ref. [<a href="#B97-coatings-13-01100" class="html-bibr">97</a>]. Copyright 2014, Royal Society of Chemistry.</p>
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<p>TEM images of the Mg-VF<sub>3</sub> powder (<b>a</b>), the SAED pattern (<b>b</b>), and the HRTEM image (<b>c</b>). A micrograph of the hydrogenated Mg−VF<sub>3</sub> powder (<b>d</b>), the SAED pattern (<b>e</b>), and the HRTEM image (<b>f</b>). Reprinted with permission from Ref. [<a href="#B99-coatings-13-01100" class="html-bibr">99</a>]. Copyright 2017, Elsevier.</p>
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<p>DTA curve of Mg−TM−La powder after hydrogen absorption. Reprinted with permission from Ref. [<a href="#B101-coatings-13-01100" class="html-bibr">101</a>]. Copyright 2013, Elsevier.</p>
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<p>SEM images of pure Mg powder (<b>a</b>), Mg@Ti (<b>b</b>), and Mg@Ti@Ni composites (<b>c</b>). Reprinted with permission from Ref. [<a href="#B102-coatings-13-01100" class="html-bibr">102</a>]. Copyright 2017, Elsevier.</p>
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<p>BF−STEM and HRTEM images of Mg@Ti (<b>a</b>,<b>b</b>) and Mg@Ti@Ni (<b>c</b>,<b>d</b>) composites after hydrogen absorption. Reprinted with permission from Ref. [<a href="#B102-coatings-13-01100" class="html-bibr">102</a>]. Copyright 2017, Elsevier.</p>
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<p>The peak dehydrogenation temperature of different materials and synergistic effects present in Mg@Ti@Ni composites. Reprinted with permission from Ref. [<a href="#B102-coatings-13-01100" class="html-bibr">102</a>]. Copyright 2017, Elsevier.</p>
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<p>A schematic of high−capacity Mg NCs encapsulated by a selectively gas−permeable polymer (<b>a</b>), the synthesis of Mg NCs/PMMA nanocomposites (<b>b</b>). Reprinted with permission from Ref. [<a href="#B104-coatings-13-01100" class="html-bibr">104</a>]. Copyright 2011, Springer Nature.</p>
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<p>Schematic illustration of a Ni-MH battery (<b>a</b>) and radar chart comparison of AB<sub>2</sub>-type, AB<sub>5</sub>-type, and RE-Mg-Ni-based hydrogen storage alloys (<b>b</b>). Reprinted with permission from Ref. [<a href="#B108-coatings-13-01100" class="html-bibr">108</a>]. Copyright 2021, KeAi Publishing.</p>
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<p>Formation of alloy surface coating. Reprinted with permission from Ref. [<a href="#B131-coatings-13-01100" class="html-bibr">131</a>]. Copyright 2017, Elsevier.</p>
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<p>Morphology of alloy powders before and after electroless plating. (<b>a</b>) Untreated alloy SEM; (<b>b</b>) Ni-coated alloy SEM; (<b>c</b>) Co-coated alloy SEM. (<b>d</b>) Untreated alloy TEM; (<b>e</b>) Ni-coated alloy TEM; (<b>f</b>) Co-coated alloy TEM. Reprinted with permission from Ref. [<a href="#B131-coatings-13-01100" class="html-bibr">131</a>]. Copyright 2017, Elsevier.</p>
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<p>The preparation process of rGO−Mg<sub>2</sub>Ni: (<b>a</b>) APS modification; (<b>b</b>) electrostatic self-assembly. Reprinted with permission from Ref. [<a href="#B132-coatings-13-01100" class="html-bibr">132</a>]. Copyright 2017, American Chemical Society.</p>
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<p>Tafel polarization curves of the bare Mg<sub>2</sub>Ni alloy and rGO−Mg<sub>2</sub>Ni composite electrodes (scan rate: 1 mV s<sup>−1</sup>). Reprinted with permission from Ref. [<a href="#B132-coatings-13-01100" class="html-bibr">132</a>]. Copyright 2017, American Chemical Society.</p>
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<p>Evolution of the discharge capacity of the as-milled La<sub>9</sub>Ce<sub>1</sub>Mg<sub>80</sub>Ni<sub>5</sub> + 200 wt% Ni + <span class="html-italic">x</span> wt% GR (<span class="html-italic">x</span> = 0–4) with cycle number: (<b>a</b>) Milling for 20 h, (<b>b</b>) milling for 80 h. Reprinted with permission from Ref. [<a href="#B140-coatings-13-01100" class="html-bibr">140</a>]. Copyright 2020, Elsevier.</p>
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<p>Tafel (<b>a</b>) and cyclic voltammetry curves (<b>b</b>) of the alloys. Reprinted with permission from Ref. [<a href="#B151-coatings-13-01100" class="html-bibr">151</a>]. Copyright 2020, Elsevier.</p>
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<p>The cyclic life curves (<b>a</b>) and the cyclic voltammogram (CV) curves (<b>b</b>) of the La<sub>0.7</sub>Mg<sub>0.3</sub>Ni<sub>2.4</sub>Co<sub>0.6</sub> alloy electrodes. Reprinted with permission from Ref. [<a href="#B155-coatings-13-01100" class="html-bibr">155</a>]. Copyright 2008, Elsevier.</p>
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14 pages, 8326 KiB  
Article
The Effect of C45 Carbon Black-Phosphomolybdic Acid Nanocomposite on Hydrogenation and Corrosion Resistance of La2Ni9Co Hydrogen Storage Alloy
by Krystyna Giza, Edyta Owczarek and Andrzej Miszczyk
Energies 2023, 16(10), 4002; https://doi.org/10.3390/en16104002 - 10 May 2023
Cited by 1 | Viewed by 1622
Abstract
In this paper, we analysed the influence of corrosion processes and the addition of a carbon black-heteropoly phosphomolybdic acid (C45-MPA) nanocomposite on the operating parameters of a hydride electrode obtained on the basis of the intermetallic compound La2Ni9Co. The [...] Read more.
In this paper, we analysed the influence of corrosion processes and the addition of a carbon black-heteropoly phosphomolybdic acid (C45-MPA) nanocomposite on the operating parameters of a hydride electrode obtained on the basis of the intermetallic compound La2Ni9Co. The electrochemical properties of negative electrodes for NiMH batteries were studied using galvanostatic charge/discharge curves, the potentiostatic method, and electrochemical impedance spectroscopy (EIS). The morphology and chemical composition analysis of the studied electrodes were investigated by means of scanning electron microscopy (SEM) with supporting energy-dispersive X-ray analysis (EDS). For more structural information, FTIR analysis was performed. The results indicate that the presence of the C45-MPA nanocomposite in the electrode material increased both the discharge capacity of the hydride electrode and the exchange current density of the H2O/H2 system. The heteropoly acid-modified electrode is also more resistant to high discharge current densities due to its catalytic activity. Full article
(This article belongs to the Section A5: Hydrogen Energy)
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Figure 1

Figure 1
<p>Results of SEM–EDX qualitative analysis of C45 carbon black (<b>a</b>) and C45-MPA (<b>b</b>).</p>
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<p>FTIR spectra of C45 carbon black (a), C45-MPA (b), and MPA (c).</p>
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<p>Cyclic voltammograms recorded at scan rate of 10 mV s<sup>−1</sup>.</p>
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<p>Galvanostatic charge/discharge curves (<b>a</b>); discharge capacity and exchange current density as a function of number of cycles (<b>b</b>).</p>
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<p>Open circuit potential versus SCE for La<sub>2</sub>Ni<sub>9</sub>Co and La<sub>2</sub>Ni<sub>9</sub>Co-MPA electrodes before and after cycling.</p>
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<p>Potentiokinetic curves for La<sub>2</sub>Ni<sub>9</sub>Co and La<sub>2</sub>Ni<sub>9</sub>Co-MPA electrodes before and after cycling recorded at scan rate of 1 mV s<sup>−1</sup>.</p>
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<p>Galvanostatic charge/discharge curves (<b>a</b>); discharge capacity and exchange current density as a function of discharge current density (<b>b</b>).</p>
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<p>SEM micrographs of La<sub>2</sub>Ni<sub>9</sub>Co (<b>a</b>) and La<sub>2</sub>Ni<sub>9</sub>Co-MPA (<b>b</b>) composite electrodes after activation and results of EDS analysis.</p>
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<p>Impedance spectra measured for studied electrodes after 24 h of immersion in 6 M KOH solution. Experimental data: 6 M KOH, 25 °C, frequency range: 100 kHz to 0.01 Hz, amplitude: 5 mV.</p>
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<p>Schematic impedance spectra of porous electrode in Nyquist format according to de Levie with same pores (<b>a</b>), with distribution of pore dimensions (<b>b</b>), and with fractal pores (<b>c</b>).</p>
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<p>Schematic diagram of electrode with same example pores (<b>a</b>), distribution of pores (<b>b</b>), fractal pores with primary level of porosity (<b>c</b>), and fractal pores with primary and secondary levels of porosity (<b>d</b>).</p>
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<p>Impedance spectra measured for studied electrodes after ten charge/discharge cycles. Experimental data: 6 M KOH, 25 °C, frequency range: 100 kHz to 0.01 Hz, amplitude: 5 mV.</p>
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