Simulation of Ni-MH Batteries via an Equivalent Circuit Model for Energy Storage Applications

Zhu, Ying; Zhu, Wenhua H.; Davis, Zenda; Tatarchuk, Bruce J.

doi:https://doi.org/10.1155/2016/4584781

Advances in Physical Chemistry

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Abstract Introduction Experimental Results and Discussion Conclusion Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2016 | Article ID 4584781 | https://doi.org/10.1155/2016/4584781

Simulation of Ni-MH Batteries via an Equivalent Circuit Model for Energy Storage Applications

Ying Zhu,¹Wenhua H. Zhu,¹Zenda Davis,¹and Bruce J. Tatarchuk¹

Academic Editor: Claudio Fontanesi

Received21 Oct 2015

Accepted17 Jan 2016

Published16 Mar 2016

Abstract

Impedance measurement was conducted at the entire cell level for studying of the Ni-MH rechargeable batteries. An improved equivalent circuit model considering diffusion process is proposed for simulation of battery impedance data at different charge input levels. The cell capacity decay was diagnosed by analyzing the ohmic resistance, activation resistance, and mass transfer resistance of the Ni-MH cells with degraded capacity. The capacity deterioration of this type, Ni-MH cell, is considered in relation to the change of activation resistance of the nickel positive electrodes. Based on the report and surface analysis obtained from the energy dispersive X-ray spectroscopy, the composition formula of metal-hydride electrodes can be closely documented as the AB₅ type alloy and the “A” elements are recognized as lanthanum (La) and cerium (Ce). The capacity decay of the Ni-MH cell is potentially initiated due to starved electrolyte for the electrochemical reaction of active materials inside the Ni-MH battery, and the discharge product of Ni(OH)₂ at low state-of-charge level is anticipated to have more impeding effects on electrode kinetic process for higher power output and efficient energy delivery.

1. Introduction

The prosperity of rechargeable Ni-MH and Li-ion batteries rapidly commercializes their application to plug-in hybrid electric vehicles (PHEVs), hybrid electric vehicles (HEVs), and battery electric vehicles (BEVs). Li-ion batteries are in general 50% lighter in weight and 25%–30% smaller in size [1], making an easier assembly in vehicle, generating more power to boost acceleration, and increasing energy efficiency through on-board battery energy storage via regenerative braking and mechanical-electric energy conversion. A gradual capacity reduction and performance decay are inevitable based on the current knowledge of rechargeable battery technology. It is essential to monitor and control the level of state-of-charge (SoC) in consideration of operating lifetime for the rechargeable batteries. Although the Li-ion battery power packs have remarkable advantages, the on-board energy storage using Ni-MH battery packs is currently powering many of today’s hybrid vehicles on the road. This nickel-based metal-hydride battery is lighter than the traditional lead-acid one and approximately delivers twice the power output for the weight as the Pd-acid battery. The accuracy for SoC prediction is a challenge for the requirements of both battery management systems (BMS) and various EV charging infrastructure. Battery impedance is a valid tool to diagnose the cell health conditions and to assist the understanding of electrochemical reaction mechanisms. The limitation for practical applications comes from the difficulties of measurement at load and impedance data interpretation for related physical parameters and electrochemical processes. Electrochemical impedance spectroscopy (EIS) is a valid in situ nondestructive technique for battery evaluation to assess the dynamic responses at loads. It has been experimentally proven by its wide applications to various electrochemical systems, including electrodes-aqueous electrolyte interfaces [2], conducting polymers [3, 4], supercapacitors [5], solar cells [6], fuel cells [7, 8], and rechargeable batteries [9–12]. As a whole, it is valuable for further product improvement through deep understanding of the battery deterioration mechanisms during degradation process. The interpretation of impedance data can be achieved by equivalent circuit (EC) simulation and mechanistic analysis.

Characterizations through EIS impedance for NiOOH/Ni(OH)₂ electrodes [13, 14] delivered valuable contributions to the development of nickel-based alkaline rechargeable batteries. The modification of Ni electrodes [15, 16] is experienced with the abundant assistance of the EIS technique for performance improvement of Ni-MH batteries. Previously, Kuriyama et al. [17] fully developed a deterioration study of metal-hydride (MH) electrodes with impedance measurement and EC simulation. Recently, researches focused more on characterization of MH electrodes with different structures [18–20]. At the era of lead-acid (Pb-acid) and nickel cadmium (Ni-Cd) batteries, EIS had been proposed as a promising technique to monitor and determine the SoC levels of full batteries [21]. The study of Bundy et al. [22] was recognized as one of the few thorough impedance studies of full Ni-MH battery with attempt to predict the SoC values. Hammouche et al. [23] reported the impedance measurement of a 42 Ah Ni-MH pack. Half-cell impedance was measured against cell case. Later, Thele et al. [24] followed up the research on large sealed Ni-MH battery pack. Pulse load simulation and hysteresis phenomenon were utilized to validate the Ni-MH battery model. This work provided a valid reference for simulation of the Ni-MH systems by impedance analysis. Castro et al. [25] published a mathematical simulation of their lab-made Ni-MH battery based on physicochemical model. Diffusion process was considered in this model, but no fitting curves of impedance spectra were illustrated. Slepski et al. [26] used additional reference electrode to separate impedance measurement of positive and negative electrodes. An EC model of “two time constants” was suggested for the entire battery, but neither simulation process nor fitting curve was reported in detail. In this work, impedance measurement is conducted at the whole cell level for studying of the Ni-MH rechargeable batteries. An improved equivalent circuit model considering diffusion process is proposed for battery impedance data simulation at different charge input levels. The model-based impedance analysis is expected to particularly understand the battery performance deterioration at different cell health conditions and assist the mechanism diagnostics for cell capacity degradation.

2. Experimental

2.1. Rechargeable Ni-MH Cells for Testing and Evaluation

Two Ni-MH rechargeable batteries were selected for experimental measurements in this work, named as Cell A and Cell B, respectively. The batteries were sealed D-size cylindrical cells with a height of 60 mm and a diameter of 32 mm. The Ni-MH cells were originally purchased from a Radioshack® store (a division of Tandy Corp., Fort Worth, TX) in a brand new condition. The nominal voltage is labeled as 1.2 V and the nominal cell capacity is marked as 4500 mAh (Radioshack #23-519). Sealed Ni-MH batteries can generally achieve a cycle life of more than 500 charge-discharge cycles [27] with regular operation. Performance degradation was gradually occurring in the Ni-MH Cell A and Cell B due to years of charge/discharge service cycles and shelf storage. The Arbin Battery Tester (Abts 4.0 with 8 channels) was applied for battery capacity measurement and rate performance evaluation. The cell capacities of the Ni-MH Cell A and Cell B were measured at 3702 mAh and 4362 mAh at a 0.2 C rate after years of services for various laboratory duties and overcharge endurance, respectively. This means the batteries are under different state-of-health (SoH) conditions. In this work, we simply the study by using the nonidentical battery capacity at different cell health status for imitating individual cell position in the real battery power systems after long-term cycling tasks. Impedance measurement is then conducted to study the cell deterioration and capacity degradation mechanisms.

2.2. Battery Characterization by AC Impedance Spectroscopy

AC impedance is a type of EIS technique that measures the impedance of electrochemical systems by employing sinusoidal signals as electrical stimulus. To measure cell impedance at a certain capacity level, the specified amount of charge was input to the fully discharged cells at a rate of 0.2 C. As detailed in our previous work [28], the ratio of the charge input to the rated cell capacity (RoC) is defined as The value of RoC has some difference in comparison with the value of SoC after the charge input is more than . 85% SoC at a 0.2 C rate. When the specified RoC level was reached during the tests, the impedance measurement was applied to the cells under current loads. The loaded current was 370 mA for the Ni-MH Cell A and 436 mA for Cell B. The Gamry impedance monitor and TDI-Dynaload® programmable load were employed to obtain impedance spectra. The frequency swept from 10 kHz down to 0.01 Hz in each measurement. Impedance data were recorded at a rate of 5 points per decade frequency. When finishing the impedance measurement, the cells were continuously discharged to the cut-off voltage of 1.0 V at a rate of 0.2 C. In other words, the Ni-MH cells were fully discharged to a SoC level of 0% after each impedance measurement. The impedance data at a higher RoC level was measured by repeating this procedure. The proposed equivalent circuit model was utilized to simulate all measured impedance spectra through the software called Gamry Echem Analyst.

The mode of hybrid EIS was selected in this work for Ni-MH cell measurement. The EIS mode was firstly put forward as variable-amplitude Galvanostatic method when studying H-cells with copper/sea water system [29]. The Galvanostatic EIS mode is a perfectly valid technique for impedance data collection but it possibly produces a voltage outside the linear range due to the significant impedance increase. This results in the unacceptable impedance data. The hybrid EIS mode is able to overcome this problem by continually adjusting the applied excitation current during experiment. The electrochemical systems were studied under constant current density. However, the current signal applied to the testing system is regulated in the hybrid EIS mode before measurement of each data point. The signal regulation is able to yield an voltage at desired magnitude to ensure a pseudolinear behavior, and consequently the voltage does not extend beyond the linear range. The validation and accuracy of impedance measurement highly rely on the pseudolinear behavior of electrochemical systems.

During the impedance measurement in this work, a desired voltage perturbation and an estimated impedance magnitude were set before the measurement. The initial current perturbation [30] was calculated by where was the amplitude of the current perturbation superimposed on the load for measurement at the first frequency point. was the amplitude of the desired voltage perturbation, chosen as 5 mV for this specific application. The value of was the magnitude of the system impedance estimated before the measurement. The measured impedance value at this frequency point was then recorded as . The current perturbation employed for each following frequency point was calculated by [29, 30]where was the amplitude of the current perturbation used at the th measuring point and was the magnitude of the system impedance measured at the th point.

2.3. Electrode Materials Composition by Energy Dispersive X-Ray Spectroscopy

One of this type of nickel metal-hydride cell was cut and broken down to get small amount of samples from the negative electrodes for surface analysis. The electrode composition was analyzed by energy dispersive X-ray spectroscopy (EDX or EDS). The EDX surface technique is a bulk analytical technique used to qualitatively and quantitatively detect element composition. It is able to probe 3-4 m below the surface of the powder and has a sensitivity of about 1000 ppm for elements from beryllium (Be) with atomic number 4 to uranium (U) with atomic number 92. The electrode samples were powdered and pressed into double-sided C tape on the EDX specimen mount. The composition of metal alloy used for the negative electrodes was detected by identifying the metal elements and their percentage.

3. Results and Discussion

3.1. Electrode Compositions

The formulas of metal-hydride alloys used for the negative electrode of the Ni-MH batteries basically follow the disordered AB₅ type, A₂B₇ type, or disordered AB₂ type [31]. The typical elements on “A” sites and “B” sites are different in various alloy types; however, “A” generally refers to rare earth mixture and “B” refers to transition metals. According to Ovshinsky’s valuable work on the MH negative electrodes for Ni-MH batteries [32], the disordered AB₅-type mischmetal (Mm) alloy [18–20] has been developed to be available for the most commercial use performing better cycle ability than other alloy structures. In this work, EDX reported that the electrode samples approximately follow the atomic ratio of AB₅ as shown in Figure 1. The “A” type elements include lanthanum (La) and cerium (Ce). The “B” type elements include nickel (Ni), cobalt (Co), aluminum (Al), and manganese (Mn) with the primary component of Ni. Small amount of potassium (K) was also detected in the analytic process. This results from the use of KOH electrolyte during assembling of the Ni-MH cell. The element of Mn is able to adjust the metal-hydrogen bond strength [32], and the existence of Al and Co significantly promoted electrode kinetics [31, 32]. Based on the EDX report and analysis, the formula of this AB₅-type hydride alloy can be roughly expressed as (La_9.70Ce_4.39)(Ni_60.75Co_6.66Al_3.59Mn_4.45), according to Fetcenko et al.’s work [31] on the composition of metal-hydride alloys.

3.2. Impedance Spectra and Equivalent Circuit Simulation

The Ni-MH cells became aged states after various operating tasks, and the cell capacities were measured as 3702 mAh and 4362 mAh, less than the nominal capacity of 4500 mAh as specified by the manufacturer. The capacity reduction reflects cell degradation during numerous cycling loads at ambient shelf storage conditions. This represents the state-of-health (SoH) change for individual cells. Impedance spectra of the Ni-MH cells measured at different capacity levels are illustrated in the same Nyquist plots as shown in Figure 2. The impedance arcs of both cells at higher frequency region have the arc shapes similar to depressed semicircles. Comparing the magnitudes of these impedance arcs at direction and direction, these “semicircles” are depressed to a large extent. A change of curvature can be observed clearly at higher frequency region from the impedance spectra of the Ni-MH cell (Cell A), which implies the possibility of two overlapped impedance arcs. One straight tail dominates the behavior of cell impedance at lower frequency region of both cells at all SoC levels. Despite the similar shape of impedance spectra, the total impedance of the Ni-MH Cell B is slightly larger than the value of Cell A. The impedance of Cell B also executes larger changes with increasing the charge input than the value of Cell A. The altered magnitude and behavior of impedance spectra illustrate different amount of capacity decay in two Ni-MH rechargeable cells.

A typical Randles circuit as shown in Figure 3(a) consists of one ohmic resistance, , one parallel () subcircuit behaving as a semicircle in Nyquist plot, and one Warburg element (symbolized by ) behaving as a unit slope line at the lowest frequency region [33]. This model considers faradaic impedance contributed by both kinetic reaction processes and diffusion processes. Since the depressed semicircles were observed from the impedance spectra of the Ni-MH cells, a modification to Randles circuit is necessary to be considered for the circuit model expansion and improvement.

One explanation to the depression is the existence of nonideal behaviors, usually caused by the surface roughness and varying thickness of electrodes, unevenly distributed current, and nonhomogeneous reaction rate. A generalized element, constant phase element (CPE, symbolized by ), can be used to replace ideal physical elements in the case of nonideal behaviors. The phase angle of CPE remains constant through all the frequency range [34]. The impedance of a CPE [33] can be written as The exponential number reflects the degree of nonideality. When the value of in (4) equals 1, 0, −1, and 0.5, this equation turns out to be the expression of pure capacitor , pure resistor , pure inductor , and Warburg element, respectively. To simulate the nonideal capacitive behavior, the value of needs to be limited between 0.8 and 1.0 [33]. With this valid restriction, one () failed to simulate the impedance arcs at higher frequency region. In this case, the overlap of two semicircles is preferred to explain the large extent depression. One more parallel () subcircuit (Figure 3(b)) was added into a series with the Randles circuit to derive the ideal equivalent circuit model (Figure 3(c)) for studying of the full Ni-MH cells. To improve the fitness of the equivalent circuit model to the experimental data, nonideal processes are essential to be considered for the Ni-MH cells. In this work, the ideal equivalent circuit model in Figure 3(c) was further modified to the nonideal equivalent circuit model as shown in Figure 4. It is an improved equivalent circuit model in this work proposed for the following simulation efforts. Three CPEs were applied to replace two ideal capacitors and one Warburg element for nonideal capacitive behaviors and nonideal diffusion behavior. The simulation fitness of this nonideal improved model to the experimental data measured in this work is illustrated as shown in Figure 5. The impedance spectrum measured from the Ni-MH cell at a capacity level of . 30% SoC (dots) was plotted to detail the fitness of simulation curve (solid line). The pure resistor refers to the smaller intercept of impedance spectra in real axis. Two parallel subcircuits ( and ) are applied to simulate two overlapping impedance arcs in higher frequency range. For nonideal capacitive behavior, the exponential numbers of and are expected to stay between 0.8 and 1.0. The element simulates the straight lines in the low frequency range for the nonideal Warburg behavior with an exponential number slightly less than 0.5. The simulation result from the fitting curves presents good consistency with measurement data.

Kuriyama et al. [17] proposed an equivalent circuit model of “four time constants” for the MH electrodes. The model consisted of three () parallel circuits and one Warburg element. The fitting values of model elements were utilized to study the deterioration mechanism of electrodes without showing the fitting curves. However, equivalent circuit models having less time constants were preferred to avoid redundancy. An equivalent circuit model with diffusion element of “three time constants” [20] was developed by Tliha et al. to simulate their AB₅-type MH electrodes at altered SoC levels. The mature research on NiOOH/Ni(OH)₂ electrodes confirmed that an equivalent circuit model consisted of one () parallel circuit and one diffusion circuit [13]/diffusion element [35] was capable of providing excellent electrode simulation. Slepski et al. [26] suggested an equivalent circuit model of “one time constant” for their positive electrode and an equivalent circuit model of “two time constants” for their negative electrode. However, the suggested equivalent circuit model only had two time constants. No diffusion element was considered either in electrode models or in full battery model. In this work, the proposed nonideal equivalent circuit model has three time constants with consideration of diffusion processes. The impedance spectra of positive and negative electrode overlapped to some extent at higher frequency region; however, two () subcircuits were preferred to distinguish contributions from each electrode.

The simulation results of the Ni-MH Cell A and Cell B at different RoC levels are shown in Figures 6 and 7. In higher frequency range, the two parallel () circuits simulate the measured impedance spectra quite well under all cell status. However, the fitting curves gradually deviate from the impedance data when the frequency decreases to lower than 1 Hz. This deviation becomes more significant at higher charge input levels, especially at 100% RoC level. Mathematical models likely implement better simulation in this frequency region than semiempirical EC models [25]. Other impedance studies of full Ni-MH cells [22, 23, 26] paid more attention to measurement data and SoC studies. Valoen et al. [36] reported an improvement of simulation at low frequency region by considering hydrogen evolution process; however, this work was done merely for MH electrodes but not for full Ni-MH cells. As a whole, the simulation curves are basically identical with the measured experimental data.

(a)

(b)

(c)

(d)

3.3. Interpretation for Equivalent Circuit Elements

The understanding of cell mechanisms can be obtained through equivalent circuit simulation in addition to proper interpretation for physical elements and electrochemical processes. The electrolyte of Ni-MH rechargeable batteries is usually a concentrated potassium hydroxide (KOH) solution. The whole discharge process [27] can be described by the following electrochemical reaction asThe reactant of nickel oxyhydroxide (NiOOH) refers to the active material of positive electrodes. Hydrogen is absorbed into metal alloys during the cell charge process and the reactant of MH refers to the metal hydride alloy at the negative electrodes after charging. The overall reaction of the charging process is simply the reversing process of (5). However, Karden et al. [37] demonstrated that the electrode kinetics is an asymmetric process during charge and discharge for a 12 V Pb-acid battery. Batteries potentially undertake different impedance spectra during charging process in comparison to discharging process under the same operating condition. The mechanisms discussed below for the Ni-MH cells are for better understanding of the discharging processes at different RoC levels.

3.3.1. Mechanism on Negative Electrodes

The half-cell process on the negative electrode is called the dehydriding reaction [38]. It can be expressed as follows:(a)Hydrogen atoms adsorbed in metal alloy transfer from bulk sites to surface sites. These are metal alloy sites at the interface of electrode and electrolyte, described as where refers to the hydrogen atom adsorbed in the metal alloy; and refer to the empty sites of metal alloy on surface and in bulk, respectively. Vitanen [39] explained this process as hydrogen released from the hydride phase to form adsorbed hydrogen atoms.(b)Hydrogen oxidation reaction (HOR) at the electrode/electrolyte interface is a charge transfer step coupled by the diffusion process of hydroxide ions from bulk electrolyte to the electrode/electrolyte interface. It is represented by where and refer to the hydroxide ions in the bulk of electrolyte and at the interface of electrode/electrolyte, respectively; is water atoms produced by the HOR process at the electrode/electrolyte interface.(c)Transport of water molecules away from electrode/electrolyte interface to bulk electrolyte can be expressed with the following reaction:where is water molecules in bulk electrolyte.

The rate-limiting step on the negative electrode is the one-electron transfer kinetic process (see (8)) when there are sufficient hydrogen atoms adsorbed in the metal alloy sites on electrode surface. Diffusion of hydrogen atoms from bulk electrode to surface sites (see (6)) is a semi-infinite diffusion process featured by Warburg behavior at low frequency. This process does not have significant effect on cell impedance under common conditions [18, 38] but will become the rate-limiting process at low temperature [40] due to decrease of diffusion coefficient. The mass transfer process of hydroxide ions (see (7)) from bulk electrolyte to electrolyte/electrode interface is a porous bounded diffusion process. Its impedance effect can be negligible under general conditions but becomes significant under a large current load. The rate of hydroxide ion diffusion process lags behind the electrode kinetics at large current loads. The transfer process of water molecules (see (9)) can be neglected when compared to other processes, because the hydroxide ion concentration in electrolyte is assumed to be large enough [38] and globally constant during battery operation [23].

3.3.2. Mechanism on Positive Electrodes

Zimmerman and Effa [14] proposed a mechanism for the discharge process of NiOOH/Ni(OH)₂ electrodes. Following this recommended mechanism, the step-by-step reaction can be summarized as follows:(a)Transport process of water molecules from bulk electrolyte to the interface of electrolyte and electrode, followed by the formation of proton at catalytic site at the interface, is described by the following reactions: (b)Transport process of hydroxide ions from the interface back to the electrolyte bulk is written as (c)Electrode reduction reaction of NiOOH active material, which is a charge transfer process coupled by the diffusion process of proton from the surface site to the charge transfer site in the electrode bulk, is expressed with the following reaction steps:The processes on positive electrodes are different from what is discussed above for the negative electrodes. Diffusion process is considered as the rate-limiting step. Its effect on NiOOH/Ni(OH)₂ electrode can be observed under general battery operating conditions [14]. This means that the charge transfer process expressed as (14) is not the rate-limiting process. And the diffusion process of proton in positive electrode (see (13)) is considered as the rate-limiting step under normal discharge process. The impedance of proton diffusion process can be applied to simulate the Warburg behavior.

3.3.3. Full Battery Impedance

The impedance arcs of semi-infinite diffusion processes were observed from impedance spectra of both MH electrodes [17–20] and NiOOH/Ni(OH)₂ electrode studies [13, 15, 16, 35]. However, only one Warburg behavior arc was observed at low frequency region in this work. Thus, the difficulty of interpretation lies in the diffusion process. Karden et al. [37] measured the half-cell impedance separately and compared the sum of the half-cell impedance to the total cell impedance. The comparison clearly illustrated that the negative electrode impedance dominated higher frequency region and the positive electrode contributed to the diffusion impedance in lower frequency region. Hammouche et al. [23] also reported that the nickel hydroxide electrode contributed the diffusion impedance to the full cell under normal discharge conditions. Based on the discussion of half-cell mechanism in the previous section, the diffusion element simulates the rate-limiting diffusion process of positive electrode. It is explained as the solid-state diffusion process of proton in nickel hydroxide electrode expressed as (13). The parallel subcircuit (), connecting to the diffusion element, simulates the charge transfer process occurring on the electrolyte/positive electrode interface coupling with the reduction reaction of the active material NiOOH (see (14)). And the parallel subcircuit () is ascribed to the one-electron transfer process of HOR occurring on the surface of the negative electrode. The pure resistor , connecting in series to other equivalent circuit elements, simulates the ohmic resistance. It consists of the resistance of cell components (electrodes, electrolyte, and conducting substrates) and resistance introduced by contact and connection.

3.4. Changes of Ohmic and Charge Transfer Resistances

The correlation between RoC and SoC was studied on the Ni-MH cell (Cell B) [28]. When certain amount of charge input was applied to Cell B, its value of RoC was calculated based on the amount of charge. The SoC level was determined when Cell B was discharged to 1.00 V cut-off voltage at a 0.2 C rate. Based on the test and calculation results, the values of RoC are identical to the SoC parameter when the capacity level is below . 85% SoC. As the value of RoC continues to linearly increase with the amount of charge input, the rate of the SoC increase gradually slows down. The values of SoC deviate from RoC at a higher capacity level, but the difference starts at the beginning with a small magnitude. The reason is that the side reaction of oxygen reduction reaction (ORR) which occurred on the positive electrode (see (15)) competes for the amount of charge input. To protect Ni-MH batteries under the overcharge condition, the capacity of negative electrodes is usually designed as 1.5 to 2 times that of positive electrodes [27]. After evolving on the positive electrode, oxygen diffuses through the separators with unsaturated electrolyte and reaches the negative electrode to recombine with water molecules (see (16)). The side reactions on both electrodes during overcharge [27] can be expressed as follows: Overcharge at positive electrodes: Overcharge at negative electrodes: Side reactions also compete with cell reactions when the operation falls into overdischarge conditions at low capacity levels and are simply described as follows: Overdischarge at positive electrodes: Overdischarge at negative electrodes: Hydrogen transfers from the positive electrode to the negative electrode through the separators with unsaturated electrolyte. Side reactions consume the charge energy without changing electrolyte and electrodes under overcharge and overdischarge conditions. In this way, the Ni-MH cells are balanced but cell energy efficiency drops to a lower level. However, it is preferred to avoid these overcharge and overdischarge operating windows because the oxidation reactions are harmful to the battery material durability and shorten the cell operating lifetime. Nelson pointed out that the realistic operation window for hybrid driving duty cycle of HEVs was from 30% SoC to 70% SoC [41]. When studying the battery mechanism and capacity decay, this work chooses more tests for the impedance measured at the operating window between 30% and 70% SoC, equivalent to the same values of RoC.

The change of ohmic resistance and charge transfer resistance with charge input levels is shown in Figures 8–10. The resistances of the Ni-MH Cell A and Cell B contributed by the same processes are plotted on the same figure for comparison. The ohmic resistance of Cell A stays at a lower and more stable level than Cell B (Figure 8). Between the capacity levels from 20% to 100% RoC, the value of of Cell B slightly increases with increasing the charge input level likely due to temporary water formation inside the positive electrodes. This potentially results in the changes of local electrolyte concentration and the battery equivalent series resistance . However, this expected variation is not obviously shown in the Ni-MH Cell A. More concentrated KOH electrolyte likely contributes to this lower equivalent series resistance for Cell A. The status of electrolyte and any other auxiliary components such as electrode material status for hydrogen storage capability also likely contribute to the value change of parameter.

The charge transfer resistance contributed by the HOR process on negative electrodes () is plotted against the charge input levels as shown in Figure 9. The cell parameter of is relatively stable with increasing charge input levels. of both cells stay at a similar value, which means the electrode kinetics of HOR process on negative electrodes of both cells are equivalent to each other. Although the cell capacities of two cells are different after aging processes, the capacity of negative electrodes is designed at a sufficient level for cell protection. The reduction of cell capacity available is not contributed by the negative electrodes due to a relative stable charge transfer resistance showing the identical negative HOR kinetics.

The Ni-MH cell capacity available is dominated by the amount of capacity at the positive electrode. A visible difference exists between the charge transfer resistances contributed by the positive electrodes () of two Ni-MH cells at different state-of-health levels after years of providing electrical power services through numerous charge and discharge cycles (Figure 10). The Ni-MH Cell B has a relatively more stable in comparison with that of Cell A, because more active materials available for cell discharge are kept at the positive electrode of Cell B, corresponding to faster kinetics and higher electrode capacity. The more cell capacity available for Cell B can be reflected by smaller charge transfer resistance at its positive electrode (). As a result of experimental measurement, the cell capacity of the Ni-MH Cell A after aging process is measured at about 3702 mAh, much smaller than the amount of 4362 mAh capacity for Cell B. The positive electrode of Cell A is more degraded compared to Cell B, likely due to limitation of insufficient amount of aqueous KOH supply, that is, starved electrolyte for the electrochemical reaction of active materials inside the battery. Additionally, the product of Ni(OH)₂ at a low level of SoC is estimated to have more impeding effects on electrode kinetic process for energy conversion and delivery (see (14)). Thus, the value of of the Ni-MH Cell A presents a slightly more increase with decreasing the charge input level (RoC) as expected. The discrimination and interpretation of impedance spectra illustrate that the impedance difference between the Ni-MH cells at different health status resulted firstly from the difference of ohmic resistances and secondly from the active material difference available for NiOOH reduction reactions on the positive electrodes inside the Ni-MH cells.

4. Conclusion

In this work, measurement using electrochemical impedance spectroscopy (EIS), simulation through an improved equivalent circuit model (ECM), and energy dispersive X-ray spectroscopy (EDX) were applied together to characterize Ni-MH rechargeable batteries via an improved equivalent circuit model to examine and analyze chemical reaction mechanisms in the Ni-MH cells. The cell performance degraded due to altered load conditions and various power cycle services. A nonideal equivalent circuit model was derived to simulate impedance spectra measured from both cells at different capacity levels. The significant performance differences were observed from their impedance spectra and equivalent circuit simulation after the cell-aging process. The simulation through the equivalent circuit model broke down the total cell impedance into several parts, corresponding to the real physical elements and chemical reaction steps. Based on the analysis of battery chemistry, the simulation results are interpreted as the ohmic resistance, the impedance of electron transfer process of hydrogen oxidation reaction (HOR) on the negative electrode, the impedance of charge transfer process of NiOOH reduction process on the positive electrode, and the impedance of solid-state diffusion process on the positive electrode.

The Ni-MH cells studied in this work were at different health status. Their impedance spectra were measured at different charge input levels during discharging process. The ohmic resistance of the Ni-MH Cell A stayed at a slightly lower and more stable level. It is likely contributed by more concentrated KOH electrolyte. The activation resistances on the negative MH electrodes of both Ni-MH cells are basically identical in spite of the amount of charge input increase for the battery. The Ni-MH Cell A had more capacity degradation than that of Cell B, prominently reflected by the activation resistance of the positive electrode inside the cell structure. This work reveals that the impedance tool combined with equivalent circuit simulation is an effective technique to study the effect of the capacity degradation on the battery energy storage and perform battery diagnostics through the electrode reactions and mechanism analysis. It is valuable for further understanding of the Ni-MH power system failure after the battery years of service at different loads, power levels, and ambient temperature conditions, highly beneficial to the extensive product improvement, enhancement of battery management systems, and charging infrastructures for better energy harvest on-board with extended service-life cycles.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

This work was performed under a US Army contract at Auburn University (W56HZV-05-C0686) administered through TARDEC. The authors would like to thank Mr. Dwight Cahela, Mrs. Kimberly Dennis, and all CM3 group members for their assistance and contribution to this work.

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