Electroactive Polymer for Controlling Overcharge in Lithium-Ion Batteries
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1 PSI-SR-1261 Electroactive Polymer for Controlling Overcharge in Lithium-Ion Batteries A. Newman R. Pawle K. White J. Lennhoff A. Newman, R. Pawle, K. White, J. Lennhoff, "Electroactive Polymer for Controlling Overcharge in Lithium-Ion Batteries," presented at 42nd Power Sources Conference (Philadelphia, PA), (12-15 June2006). Copyright 2006 Physical Sciences Inc. All rights reserved Downloaded from the Physical Sciences Inc. Library. Abstract available at
2 Electroactive Polymer for Controlling Overcharge in Lithium-Ion Batteries A. Newman, R. Pawle, K. White, and J. Lennhoff Physical Sciences Inc. 20 New England Business Center Andover, MA tel ; fax Abstract: Lithium-ion cells placed in series are prone to overcharging, leading to shortened cycle life. The current method of control is expensive, yet ineffective, external control circuitry. We have addressed this problem by developing an alternative separator that reversibly becomes conductive when a cell reaches an overvoltage condition, shunting electrons between the electrodes at current densities up to 10 ma/cm 2. At cell operating voltages, the porous separator functions as a typical ion shuttle. For manufacturing concerns, the tensile yield strength of the durable film is 6.8 MPa (normalized force to film width of 0.17 N/mm). Keywords: conductive polymer; overcharge; cycle life; hybrid electric vehicle Introduction Lithium-ion cells need to be charged to a specified cut-off voltage in order to maintain safe operation and to achieve high cycle and calendar life. Generally, lithium-ion cells are used in battery packs with cells in series, e.g. laptop computers and hybrid electric vehicles. Even when cells are balanced for capacity and impedance, the capacity fade of the battery will vary. These cell to cell capacity variations result in overcharging of the low capacity cells without the additional monitoring and control circuitry. Controlling overcharge with either a redox shuttle or with an electroactive polymer have met with limited success due to voltage and current density constraints. Redox shuttles decompose at the charging voltages of commercial lithiumion cells and can not carry sufficient current [1]. Electroactive polymers have been suggested for controlling overcharge, but also have voltage and current density limitations. The polymer film switches from an insulator to a conductor upon overcharging. After the charging current is removed, the polymer returns to an insulator. This reversible process is shown in Figure 1. The shortcomings are due to the low oxidation potential and low loading of the electroactive polymer into an industry standard separator. [2]. In this work, PSI has developed a separator that contains electroactive poly(alkylthiophene) as an integral component of the separator rather than as an added polymer to an existing separator, while not compromising porosity. This technology provides higher overcharge current density shunting. Li + (a) Cell Charge V cell <4.3 (b) G-9231 Cell Overcharge V cell >4.3 Figure 1. Cell schematic for reversible electroactive polymer separator. Experimental Thin film separators, which were solvent cast, are composed of electroactive poly(alkylthiophene), binder polymer, and battery electrolyte soluble polymer. The porosity is created in-situ with selective dissolution of the soluble polymer. Electrochemical and mechanical testing of these films were performed. Coin cell-type testing uses a commercial LiCoO 2 positive versus lithium foil negative electrodes with 1M LiPF 6 in 1:1 EC:DMC electrolyte. Cyclic voltammatry (CV) was performed on poly(alkylthiophene) in flooded cell versus lithium as counter and reference. Using ASTM standard D882-02, we measured the tensile load and yield strength of the film using an Instron 4442 tensile tester [3]. Results and Discussion We have produced various formulations of experimental films that switch between insulator and conductor. The following results include thin film cyclic voltammetry, full cell testing, and film tensile testing.
3 Cyclic voltammograms were produced on candidate PATs for selecting the appropriate electroactive poly(alkylthiophene) (PAT). Figure 2 shows two types of poly(alkylthiophenes) (PAT). With the selection of the PAT, the oxidation potential can be tuned for different electrode couples. The oxidation potential difference between these two types of polymers is 500 mv. Current (ma) mV/sec PAT PAT Voltage (V vs. Li/Li+) H-7588 Figure 2. Cyclic Voltammogram for two types of PAT. aprotic solvent. Due to the polymer blend s limited solubility, multiple passes of solution were cast to build the separator film. The number of passes should be kept to a minimum in order to ensure a conductive pathway through the separator. Figure 4 shows an example for sample. The in-situ created open structure, an electrolyte conduit, is formed by the dissolution of one of the three polymers in the film. Current (µm) Voltage (V vs. Li/Li+) Figure 3. Poly(alkylthiophene) CV. H-7589 PAT1 is the conductive polymer used for making the separator due to its higher oxidation potential. Sample PAT2 with a lower oxidation potential is more conductive, as indicated by the larger measured current, while testing at the same scan rate of 1 mv/sec. PAT1 was selected for the formulation studies. Table 1 lists the experimental formulations investigated and their sample identification. Table 1. Sample Descriptions Sample ID 3XPT 4XPT 5XPT Relative PAT Level Base level of PAT 3 x PAT 4 x PAT 5 x PAT Figure 4. Cross-section of film. Figure 3 shows the CV of PAT1, which is the active component of this film. Note that the oxidizing voltage is ~ 3.9 volts and the reduction peak is ~ 3.7 volts. Nevertheless, the OCV is 3.96 volts with the experimental polymer film for a fully charged cell. This higher OCV may be attributed to cell polarization across the separator that produces conditions to switch the electroactive polymer to an insulator on the anode side of the separator. In addition, the finely distributed electroactive polymer may be more electrochemically addressable, i.e. improved kinetics, than the fully dense thin film on the Pt. The fabrication of this experimental separator involves dissolving the three component polymer blend in a polar Scanning electron microscopy (SEM) images show the cross-sectional microstructure of the film. The crosssectioned sample of the separator film was mounted in epoxy and polished. The conductive pathway is provided by the elongated regions of the electroactive polymer. Porosity will be formed in the balance of the film where this two-phase region contains the binder and electrolytesoluble polymer. The thickness of this cross-sectioned film is 18 µm. Fabricated separators range in thickness from 12 µm to 30 µm. Overcharging of the experimental film and an industry standard separator, for comparison purposes, result in the voltage plots shown in Figure 5. The sustained overcharge
4 current density is 6 ma/cm 2, while redox shuttles perform at less than 2.3 ma/cm 2 [4]. This lower voltage on overcharging will improve cycle and calendar life. The voltage of the industry standard separator peaks at 4.8 V. The drop in voltage is attributed to corrosion of the components within the cell, either on the cathode or anode. Cell Voltage Industry Standard Separator 3XPT Time (min) H-7591 Figure 5. Overcharge voltages at 6 ma/cm 2. Figure 6 shows the voltages of fully charged cells after applying current densities in the range from 2 ma/cm 2 to 10 ma/cm 2 at 5 minutes for each current density. The current density, experienced by the electrodes in an HEV battery pack, during pulse charging is expected to be lower than 10 ma/cm 2. All of the samples performed at advantageously lower voltages than the industry standard separator except sample 5XPT. This sample s microstructure may have limited porosity or lack a conductive pathway. Voltage XPT Industry Standard 3XPT 4XPT ma/cm 2 H-7592 Figure 6. Overcharging various separator formulations. The effect of poly(alkythiophene) (PAT) concentration in the film on the average voltage of the cell is shown in Figure 7. The 4-times concentration of PAT results in the lowest potential. As expected, adding more of the conductive phase increases the conductivity of the separator in the overcharged state. This improved conductivity results in a lowering of the cell potential. There are two benefits of having a lower potential: 1.) There is less electrochemical damage (side reactions) at the electrodes. 2.) Resistive heating will be lower. Based on the power relationship: P = i 2 R = i V, (1) where P is J/s, i is amps, R is ohms, and V is volts, ten second charging will produce a temperature rise of less than 3 C in the electrolyte-filled electrode assembly. This assumes a heat capacity of 2 J/gK for the electrode assembly. Average Voltage (V) Relative PAT Concentration Figure 7. Effect of PAT concentration. H-7593 The electrochemical performance of separator was evaluated at a C/2 discharge rate and compared to an industry standard separator, Figure 8. The lower initial voltage is attributed to potential at which the switches from a conductor to an insulator. The cell potential is lower due to higher concentration polarization created by the separator s tortuous porosity. Voltage (V vs. Li/Li+) Industry Standard Separator Capacity (Ahr) H-7594
5 Figure 8. Discharge curves.
6 The measured low capacity fade for a fully charged cell is 1%/day, which is below the 2.8% daily fade specification for the 42V USABC power assist battery. The electrical resistance of the experimental separator, in its insulative state, is compatible with industry standard separators. Figure 9 shows the discharge curves of the experimental separator at c-rates from C/10 to C/2. Within this range of testing, the electroactive separator was able to discharge to the same capacity. There is expected to be a greater challenge for this separator to perform at high rates due to its fine pore structure, but this data indicates that the separator is stable in the lithium ion cell and does not consume lithium nor collapse after 25 hours of testing for greater than six cycles. Voltage (vs Li/Li+) C/6.5 C/5 C/2.5 C/2 C/ Capacity (Ah) H-7595 Figure 9. Effect of rate on discharge capacity. The in-situ porosity of these experimental separators has higher tortuosity because of its sub-micron lenticular pores, as observed by SEM, rather than the straight-thru porosity of industry standard separators. Electrolyte mobility remains high for the experimental separator due to the decreased thickness and increased porosity. This electroactive film is 12 µm thick and 60% porous while typical separators are 25 µm thick and 37% porous. The tensile load of the electroactive separator film approaches the load required for roll-to-roll winding. Tonen Tapyrus Co. has stated in a recent patent that the film needs to be able to manage 0.2 N/mm for a separator with a width of 50 mm [5]. The tensile load for two separator films are shown in Figure 10. The yield strength of sample is 6.8 MPa, based on the load and cross-sectional area of the film. Poly(alkylthiophene) has a low tensile strength, so the addition of 4 times the loading of PAT, sample 4XPT, is expected to have a lower strength than sample. The strength of the film needs to be increased by 15%, which can be addressed by adding a more rigid polymer to increase the separator s strength. This polymer can either be the electrolyte soluble component or binder component of the film. Tensile Load (N/mm) XPT Displacement (mm) H-7596 Figure 10. Tensile load of PAT separator. In summary, these findings show that electroactive polymer separators can operate within the voltage constraints of lithium ion cells with a LiCoO 2 cathode and can carry over 10 ma/cm 2 overcharge current. We have shown that with material selection, the cut-off voltage can be tuned for the desired battery couple. In addition, this separator has the potential to carry sufficient tensile load to be processed with conventional winding equipment. Acknowledgement This work was supported by the Department of Energy, contract number FA M References 1. J. Dahn, J. Jiang, L. Moshurchak, M. Fleischauer, C. Buhrmester, and L. Krausec, J. Electrochem. Soc., 152 (6) A1283-A1289 (2005). 2. K. Thomas-Alyea, J. Newman, G. Chen, and T. Richardson, J. Electrochem. Soc., 151(4) pp A509- A521 (2004). 3. ASTM D882-02, Standard Standard Test Method for Tensile Properties of Thin Plastic Sheeting. 4. J. Dahn, J. Jiang, L. Moshurchak, M. Fleischaur, C. Buhrmester, and L. Krause, J. Electrochem. Soc., 152, pp A1283-A1289 (2005). 5. T. Kamei and M. Yamazaki, Heat-resistant Separator, US Patent No , May 4th, 2004.
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