Next Article in Journal
Half-Heusler (TiZrHf)NiSn Unileg Module with High Powder Density
Previous Article in Journal
Alginate-Based Biomaterials for Regenerative Medicine Applications
 
 
Search for Articles:
Title / Keyword
Author / Affiliation / Email
Journal
Article Type
 
 
Advanced Search
 
Section
Special Issue
Volume
Issue
Number
Page
 
Journals
Materials
Volume 6
Issue 4
10.3390/ma6041310
materials-logo
Submit to this Journal Review for this Journal Propose a Special Issue
► Article Menu

Article Menu

share Share announcement Help format_quote Cite question_answer Discuss in SciProfiles thumb_up
...
Endorse textsms
...
Comment
first_page
settings
Order Article Reprints
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Review

Lithium Ion Battery Anode Aging Mechanisms

by
Victor Agubra
and
Jeffrey Fergus
*
Materials Research and Education Center, Auburn University, 275 Wilmore Laboratories Auburn, AL 36849, USA
*
Author to whom correspondence should be addressed.
Materials 2013, 6(4), 1310-1325; https://doi.org/10.3390/ma6041310
Submission received: 27 November 2012 / Revised: 20 February 2013 / Accepted: 15 March 2013 / Published: 27 March 2013
Browse Figures
Versions Notes

Abstract

:
Degradation mechanisms such as lithium plating, growth of the passivated surface film layer on the electrodes and loss of both recyclable lithium ions and electrode material adversely affect the longevity of the lithium ion battery. The anode electrode is very vulnerable to these degradation mechanisms. In this paper, the most common aging mechanisms occurring at the anode during the operation of the lithium battery, as well as some approaches for minimizing the degradation are reviewed.

1. Introduction

The high energy/ power density, and excellent cycle life of the lithium ion battery have positioned it as the preferred portable energy source for consumer appliances and in the automotive industry. The performance of the battery depends on the development of materials for the various components of the lithium ion battery [1,2,3]. The degradation of these components during battery operation adversely affects the energy delivery of the lithium ion battery.
The various battery components undergo different aging mechanisms; the binder and electrolyte decompose, the current collector corrodes, the separator melts and corrodes, and the cathode undergoes structural disorder and metal dissolution.
The anode undergoes a multitude of aging mechanisms that degrade the electrochemical performance of the lithium ion battery. The most commonly used anode materials include carbon-based compounds and lithium-alloys. The microstructure, texture, crystallinity and morphology of the anode material directly influence its performance [4].
By design, the anode electrode has a large geometry dimension compared to the cathode electrode so as to prevent edge lithium plating at the anode ends. Also, the anode electrode generally has excess anode capacity compared to the cathode so that the battery can deliver high energy density [5]. A reduced anode capacity will polarize the anode to a potential close to lithium deposition potentials. However, higher surface area of the electrode is preferred to active surface area, since a higher surface allows short diffusion paths for lithium ions between the graphite particles; this facilitates fast charge and discharge rate and improves the capacity of the battery. Decrease particles size tends to increase the specific surface area from BET (Brunauer Emmett and Teller) method and the irreversible capacity loss increases. On the other hand, irreversible capacity decreases as the active specific area of the electrode increases. The intercalation of lithium ions into the graphite sheets at various stages, e.g., LixC6, LixC12, during the charging cycles to provide a nominal theoretical capacity of the carbon based anode of about 372 mAh/g. Additives, such as B, N and P, have been used to enhance this capacity.
Nevertheless, the anode has been associated with many aging mechanisms in the lithium ion battery. The focus of this paper is to elucidate the various aging mechanisms occurring at the anode of the lithium ion battery. Although the main focus will be on the aging mechanisms, a brief analysis of various treatment measures adopted to mitigate these aging mechanisms on the anode will be discussed.

2. Formation of Passivated Surface Layer

Graphite is one of the common anode materials for lithium ion batteries operating in organic electrolytes, such as LiPF6, with co-solvents like ethylene carbonate (EC), dimethyl carbonate (DMC), diethyl carbonate (DEC), methyl ethyl carbonate (EMC)). The reaction of the anode with the electrolyte solution in the formation stage results in the formation of species such as ROCO2Li and CO2OLi, on the anode surface. The layer formed by these species is referred to as the solid electrolyte interphase (SEI). The ROCO2Li can undergo reduction reaction with CO2 and traces of H2O in the electrolyte to form lithium carbonate [6] which further react with EC to form transesterification products such DMDOHC, EMDOHC and DECDOHC. In addition, anion contaminates, such as F− from HF and PF5, readily react with lithium to form insoluble reaction products which are non-uniform, electronically insulating, and unstable on the surface of the graphite particles [7,8,9,10,11]. In addition, the dissolution of the cathode electrode metal from the lattice into the electrolyte due to the disproportionation of Mn3+ (into Mn2+ and Mn4+) by traces of hydrofluoric acid (HF) in the electrolyte, resulting in the deposition of cation contaminates, such as of Mn, Co and Fe, on the anode electrode surface [12],
At higher battery potentials, during the intercalation of lithium ions into the anode lattice structure, the graphite anode oxidizes. At this potential, electrolyte co-solvents, such as EC, which is highly reactive, react with the lithium ions and the reaction products quickly precipitate and grow on the anode surface [13,14]. The presence of these reaction products on the surface retards the intercalation kinetics of the carbon anode [15]. The surface layer grows in thickness as the decomposition reaction continues [16,17,18,19,20,21,22]. The layer thickness is established to be a function of operating cycles, regardless of the charging protocol (i.e., pulse charging or DC charging) [23,24,25]. The layers become unstable and crack due to expansion and contraction of the graphite lattice during the insertion and de-insertion of the lithium ions [26,27,28]. This allows further surface reaction at these sites that may eventually isolate the graphite particles from the current collector. Figure 1 shows a typical surface film morphology and cracking of the layer (e.g., [26,27]). The surface crack formed on the surface does not typically travel to the carbon electrode [26]. The formation of this surface film layer is the predominate source of lithium ion loss in lithium ion battery during storage conditions [25]. It also leads to an increase in the charge transfer resistance, impedance, and clogs pores on the carbon anode electrode [29,30,31], which limits accessibility of lithium ions to the anode surface leading to an increase in irreversible capacity [32,33,34]. The growth of this surface layer on the anode electrode is prevalent in the electrolyte system with EC as the co-solvent compared to those with DEC or DMC as co-solvents [35,36,37,38].
Materials 06 01310 g001 1024
Figure 1. Growth of the passivation layer on the anode resulting from electrolyte decomposition. (a) Surface film agglomerates; (b) Surface film forms a “mat” on the carbon particle surface area.
Figure 1. Growth of the passivation layer on the anode resulting from electrolyte decomposition. (a) Surface film agglomerates; (b) Surface film forms a “mat” on the carbon particle surface area.
Materials 06 01310 g001

3. Anode Impedance

The growth of the passive surface layer on the anode creates resistance to lithium ion flow, which results in a rise in the charge transfer resistance and the impedance of the anode [39,40]. This increase in anode impedance is said to increase with charge rate, cycle number, temperature, and anode material particle size [41,42,43]. However, at low temperatures (10–30 °C) and low charge rate(C/20), the anode electrode contribution to the overall battery impedance is low. This is attributed to the small amount of the surface film formed on the electrode surface [44]. The low charge rate limits the amount of excess Li+ that is not intercalated into the electrode to react with the electrolyte [45,46]. A typical SEM micrograph of anode covered with products of electrolyte decomposition reaction products is shown in Figure 2. (e.g., [38,39,44,46,47]). Common surface reaction products formed on the anode surface include Li-alkyl carbonates, lithium carbonate species and fluorinated products. These products affect the intercalation and de-intercalation kinetics of the anode, and thus result in an increase in anode electrode impedance relative to the cathode [47,48,49].
Materials 06 01310 g002 1024
Figure 2. A typical SEM micrograph of surface film growth on the graphite particles. (a) Small precipitate of surface film on the carbon particles; (b) Precipitate thickness increases.
Figure 2. A typical SEM micrograph of surface film growth on the graphite particles. (a) Small precipitate of surface film on the carbon particles; (b) Precipitate thickness increases.
Materials 06 01310 g002
Comparing the impedance of the anode is difficult owing to the multitude of testing conditions and different anode materials used in various batteries. However, Figure 3a,b shows the impedances of the individual electrodes as well as the overall battery impedance. In these two cases, the anode contributes less to the overall battery impedance compared to the cathode. In these two cases, carbon is the anode material, while LiPF6 in EC+DMC is the electrolyte system and the operating conditions are low-to-medium temperature and low charge rate. The higher battery impedance exists at high operating temperature and charge rate, where the surface reactions are enhanced and a thicker surface film layer is formed on the electrode surface.
Materials 06 01310 g003 1024
Figure 3. (a) Anode contributing less to total battery impedance (charge rate of C/2 at room temperature) [39]; (b) Anode contributing less to total battery impedance (graphite and LiNi0.8Co0.15Al0.05O2 electrodes: 0.5C charge rate at 40 °C) [45].
Figure 3. (a) Anode contributing less to total battery impedance (charge rate of C/2 at room temperature) [39]; (b) Anode contributing less to total battery impedance (graphite and LiNi0.8Co0.15Al0.05O2 electrodes: 0.5C charge rate at 40 °C) [45].
Materials 06 01310 g003

4. Degradation Due to the Loss of Recyclable Lithium Ions

The irreversible lithium ion loss is generally attributed to two phenomena, namely: (i) solid electrolyte interface (SEI) layer formation via electrolyte decomposition at the formation stage; (ii) side reaction of lithium ion with decomposed electrolyte compounds and water (e.g., 10–1500 ppm) in the electrolyte at the later stage of the battery operation [50].
The loss and/or consumption of recyclable lithium ions at the anode by the passive layer is a major cause of the reduction in the reversible capacity of the lithium ion battery [51,52]. As the layer grows, lithium is consumed in the reaction and the increased thickness inhibits Li+ transfer, thus the lithium ions must tunnel through the layer. This phenomenon is the main degradation mechanism in fully charged batteries at storage conditions [52,53,54,55], where the electronic insulating surface layer formed clog the pores and isolate graphite particles. The irreversible lithium ion loss is also a function of the specific area of the graphite particles, since an increase in area increases the volume of reaction products [56,57]. For a graphite anode with low specific area, the charge loss is low. The electrolyte additive, vinylene carbonate (VC) is one that increases the lithium ion loss rate at the anode for the Li/coke electrode during storage (ambient temperature conditions). Because it increases the rate of SEI formation reaction at ambient temperature conditions to increase the SEI thickness. However, its beneficial effect is seen at higher temperature (35–50 °C) and higher voltages >0.4 V for Li/coke, electrode as it slows down the side reaction rate and undergoes reduction and polymerization to form poly alkyl Li-carbonate species that suppress both solvent and salt anion reduction on the anode electrode.
Similarly, in batteries stored at voltages greater than 3.6V, electrolyte oxidation at the cathode can also induce surface reaction deposits that cover the active cathode electrode area. These covered areas are insulating, which could result in a non-homogeneous local current distribution in the cathode electrode.

5. Anode Degradation Due to Structural Changes

Anode materials, such as mesosphere pitch-based carbon (MSPBC) and vapor grown carbon fibers (VGCF), have high surface area morphologies that provide large discharge capacity and high charge rate performance [4]. During battery degradation, the ordered and radial structures of the carbon electrode may become less ordered, but this structural change is not the main contributor to battery degradation [58]. Degradation can be either in the form of the lithium plating or the formation of the surface film (e.g., new XRD peaks as in Figure 4). Neither the particles size nor the lattice parameter change significantly with these degradation processes [59].
Cycling the lithium ion batteries at high C-rate and high state of charge (SOC) induces mechanical strain on the graphite lattice of the anode electrode due the steep gradient of lithium ions, and thus lattice parameter, in the particle. This mechanical strain caused by the insertion and de-insertion of the lithium ions cracks, fissures and splits the graphite particles thus making these particles less oriented as compared to the original platelets [60]. Pressed graphite particles improve the ionic conductivity with a trade off in a decreased ohmic resistance and irreversible capacity loss [61]. The nature and orientation of the graphite particles influences the reversible capacity of the anode. For instance, less-oriented graphite particles have a low reversible capacity due to more difficult lithium intercalation kinetics and to the formation of new boundaries between crystallite at which irreversible lithium ions/electrolyte interaction can occur [62,63,64,65,66]. While flake-like graphite particles have higher gravimetric capacity at higher C-rate compared to spherical particles [67]. Although the crystal structure of the anode typically does not change with aging, a change in the rhombohederal/hexagonal content during battery operation has been reported. The increase in the hexagonal content during the first and third stage of lithium ions intercalation lowers Faradic efficiency, thereby decreasing the reversible capacity of the anode [68,69,70], so ideally a high ratio of rhombohederal/hexagonal content which gives a high reversible capacity is most desired.
Materials 06 01310 g004 1024
Figure 4. Structural changes on the anode electrode from degradation. (a) Surface cracks on the sufrcae of aged anode electrode; (b) XRD spectra of aged anode electrode showing change in cystal structure (new phases).
Figure 4. Structural changes on the anode electrode from degradation. (a) Surface cracks on the sufrcae of aged anode electrode; (b) XRD spectra of aged anode electrode showing change in cystal structure (new phases).
Materials 06 01310 g004

6. Influence of Particle Size, Active Surface Area and Porosity

The size of the graphite particles in the anode greatly influences the performance of the anode. Small particles contain short diffusion paths between the graphite particles, which facilitate fast charge and discharge rate [71]. Similarly, the larger surface area of the smaller graphite particles are prone to higher internal heat generation and lithium ion are consumed during the exothermic reaction at high temperatures greater than 60 °C [72] compared to larger particles size, this leads to an increase in the irreversible capacity of the graphite electrode [73,74,75]. The area specific impedance (ASI) of the graphite particles remains constant and does not vary much with capacity of the battery until the maximum capacity is reached [76] as shown in Figure 5. In the same vein, there has not been a direct correlation between the porosity of the graphite and the reversible capacity of the anode [77]. Figure 6 is a selected plot of graphite anode porosity data for prismatic and cylindrical (1.5 V) batteries cycled at 1C. An increase in porosity decreases the active surface area, reduces the electrical path into the graphite particles and reduces the accessibility of the lithium ions into the current collector. Although the pores will accommodate a large volume of electrolyte, they serve as a reaction point during the electrolyte decomposition process.
Materials 06 01310 g005 1024
Figure 5. Effect of area specific impedance (ASI) on charge capacity [76].
Figure 5. Effect of area specific impedance (ASI) on charge capacity [76].
Materials 06 01310 g005
Materials 06 01310 g006 1024
Figure 6. Effect of anode porosity on charge capacity for prismatic cell and cylindrical cell charge at 1C at 300 cycles [77].
Figure 6. Effect of anode porosity on charge capacity for prismatic cell and cylindrical cell charge at 1C at 300 cycles [77].
Materials 06 01310 g006
The density of the graphite anode has an effect on its ability to withstand degradation under strenuous battery operating conditions. A higher anode electrode particle density decreases the porosity and by extension, the active surface area of the electrode which reduces the electrode/electrolyte contact area. Therefore the denser the graphite material, the lower the irreversible capacity [78,79]. Furthermore, increased heat generation from a denser electrode material produces gaseous species [79] at temperatures greater than 120 °C from the thermal decomposition of the SEI layer. This implies that the thermal stability of the graphite anode is strongly dependent on the particle size of the graphite electrode.

7. Metallic Lithium Plating on the Anode

Its light weight, high voltage and high energy density once made lithium metal foil the preferred anode electrode for the lithium ion battery. However, its propensity to the formation of dendrites and moss made it unattractive. In the light if this, many more anode materials have been developed to replace the lithium metal foil as an anode material. Common anode materials currently used in lithium ion batteries include graphite, coke, hard carbon and lithium titanate. Among these, the unmodified graphite electrode is most susceptible to lithium plating because of the close proximity of its reversible potential to that of Li+/Li [80,81]. Lithium plating by itself is reversible, as the plated lithium oxidizes at potential of about 100mV, a potential much lower than that of lithium de-intercalation at the anode electrode, causing a voltage overshoot during the discharge cycle (over potential) as shown in Figure 7a. Well-ordered carbon and non-graphitizable carbon have gradually replaced lithium metal as the preferred anode material for the lithium ion battery because of their superior capacity, good cycleability, lower susceptibility to lithium plating, and low electrode potential relative to Li+/Li.
Materials 06 01310 g007 1024
Figure 7. (a) Schematic current voltage over-potential caused by lithium plating [81]; (b) Lithium metal morphologies [82].
Figure 7. (a) Schematic current voltage over-potential caused by lithium plating [81]; (b) Lithium metal morphologies [82].
Materials 06 01310 g007
There are several factors that initiate the formation of metallic lithium on the surface of the anode electrode, some of these include: (1) the nature of the electrolyte (i.e., electrolyte formulations with high EC content exhibit lithium plating); (2) the ratio between anode and cathode capacities (i.e., low anode/capacity ratio will polarize the anode and promote lithium plating); (3) the operating temperature and the charge rate [i.e., low temperature (−20 °C) and high charge rate] all influence plating on the anode [81,83]. These factors affect the anode kinetics and the lithium ion diffusion rate, such that lithium plates on the surface of the electrode rather than intercalating into the lattice of the carbon.
The formed metallic lithium deposits on the graphite anode are affected by the degree of random orientation of the particles in the crystal structure in the anode material and the non-uniformity of the current distribution which is a function of diffusion and current density [84,85]. The disorientation of the particles in the graphite electrode initiates inhomogeneity in the charge distribution on the anode electrode in the third and fourth intercalation stages and results in the formation of moss-like deposits and dendrites [82,86,87]. These moss-like deposits and dendrites grow as a function of the temperature and current density between the polymer separator and the anode. As the temperature and charge rate increases, the reaction rate also increases and metallic lithium is deposited on the graphite at overcharge. Dendrites can cause the separator to disconnect and become isolated from the electrolyte and in some instances pierce through the separator. The mat of dead lithium and dendrites can cause a short circuit and thermal runway in the battery (e.g., Figure 7b). The signature of lithium plating in batteries is usually manifested as a voltage plateau on the discharge voltage profile and low columbic efficiency [88].
The vulnerability of the anode electrode to degrade rapidly has prompted research to improve its stability. Several methods have been explored, including the inclusion of stabilizing compounds into the graphite matrix, formulations of dendrite and lithium plating suppression electrolyte systems. Elements such as Sn and carbon have been dispersed on the surface of the graphite to improve the electrochemical cycling properties of the anode electrode [89,90,91,92]. Sn on the surface of carbon anode reduces the SEI resistance and the overall electrode polarization at low temperature [93]. Also Sn-graphite anode increases passivation layer conductivity. While a carbon black coating suppresses the delithiation process in the inner structure of the graphite at elevated temperature and thus improves cycle life and capacity fade [94,95].
Another category of treatment on the surface of the anode electrode is the coating of the surface with additives like AD25, AsF6, VC and by thermal oxidation of the surface of the anode [95,96]. Thermal oxidation of graphite in air increases the surface area and fractional edge sites, which increases pores size and reduces particles size [97,98,99] and thus reduces the non-homogeneity of charge distribution that cause lithium plating. The additives AD25 and AsF6 stabilize the graphite at elevated temperature and suppress the formation of metallic lithium and reduction products of the LiPF6 [20,100,101]. Lastly, mechanical compression of the graphite particles during the electrode preparation process reduces the pore size thereby reducing the non-homogeneity of the charge distribution on the electrode and improving the reversible and irreversible capacities [101].

8. Conclusions

The anode of the lithium ion battery undergoes several degradation mechanisms during aging. Lithium plating is one aging mechanism which ends the life of a battery more rapidly due to the formation and growth of lithium dendrites. The decomposition of the electrolyte and subsequent formation of the film surface layer on the anode, cause an increase in the impedance and the consumption of recyclable lithium ions. These degradation mechanisms rarely affect the crystal structure of the anode electrode. The addition of various stabilizers, robust electrolyte systems, and temperature treatment are some of the methods that have been adopted to mitigate these aging effects on the electrode. However, further improvement is still needed to build a more robust anode that can deliver high energy density and good cycleability at various operating conditions.

References

  1. Whittingham, M.S. Material challenges facing electrical energy storage. MRS Bull. 2008, 33, 411–419. [Google Scholar] [CrossRef]
  2. Patil, A.; Patil, V.; Shin, W.D.; Choi, J.W.; Paik, D.S.; Yoon, J. Issues and challenges facing rechargeable thin film lithium batteries. Mater. Res. Bull. 2008, 43, 1913–1942. [Google Scholar] [CrossRef]
  3. Shukla, A.K.; Kumar, T.P. Materials for the next generation lithium ion batteries. Curr. Sci. 2008, 94, 314–331. [Google Scholar]
  4. Endo, M.; Kim, C.; Nishimura, K.; Fujino, T.; Miyashita, K. Recent development of carbon materials for Li Ion batteries. Carbon 2000, 38, 183–197. [Google Scholar] [CrossRef]
  5. Stewart, S.; Newman, J. Measuring the salt activity coefficient in Lithium-battery electrolytes. J. Electrochem. Soc. 2008, 155, A458–A463. [Google Scholar] [CrossRef]
  6. Lu, M.; Cheng, H.; Yang, Y. A comparison of solid electrolyte interphase on the artificial graphite anode of the aged and cycled commercial lithium ion cells. Eelectrochim. Acta 2008, 53, 3539–3546. [Google Scholar] [CrossRef]
  7. Belharouak, I.; Koening, G., Jr.; Tan, T.; Yumoto, H.; Ota, N. Performance degradation and gassing of Li4Ti5O12/LiMn2O4 lithium-ion cells. J. Electrochem. Soc. 2012, 159, 1165–1170. [Google Scholar] [CrossRef]
  8. Levi, M.D.; Wang, C.; Gnanara, J.S.; Aurbach, D. Electrochemical behavior of graphite anode at elevated temperature in organic carbonate solution. J. Power Sources 2003, 119, 538–542. [Google Scholar] [CrossRef]
  9. Ramadass, P.; Haran, B; White, R; Popov, B N. Capacity fade of Sony 18650 cells cycled at elevated temperatures Part I. Cycling performance. J. Power Sources 2002, 112, 606–613. [Google Scholar] [CrossRef]
  10. Haran, B.; White, R.; Popov, B.N. Capacity fade of Sony 18650 cells cycled at elevated temperatures Part II. Capacity fade analysis. J. Power Sources 2002, 112, 614–620. [Google Scholar] [CrossRef]
  11. Zhang, Y.; Wang, C.; Tang, X. Cycling degradation of automotive LiFePO4 lithium-ion battery. J. Power Sources 2011, 196, 1513–1520. [Google Scholar] [CrossRef]
  12. Yang, L.; Takahashi, M.; Wang, B. A study on capacity fading of lithium-ion battery with a manganese positive electrode during cycling. Electrochim. Acta 2006, 51, 3228–3234. [Google Scholar] [CrossRef]
  13. Smith, A.J.; Hannah, M.; Dahn, J.R. Long-term low rate cycling of LiCoO2 graphite Li-ion cells at 55 °C. J. Electrochem. Soc. 2012, 159, 705–710. [Google Scholar] [CrossRef]
  14. Abraham, D.P.; Reynolds, E.M.; Samman, E.; Jansen, A.N.; Dees, D.W. Aging characteristics of high-power lithium ion cells with LiNi0.8Co0.15Al0.05O2 and Li4/3Ti5/3O4 electrodes. Electrochim. Acta 2005, 51, 502–510. [Google Scholar] [CrossRef]
  15. Ochida, M.; Domi, Y.; Doi, T.; Tsubouchi, S.; Nakagawa, H.; Yamanaka, T.; Abe, T.; Ogumi, Z. Influence of manganese dissolution on the degradation of surface films on edge plane graphite negative -electrodes in lithium -ion batteries. J. Electrochem. Soc. 2012, 159, A961–A966. [Google Scholar] [CrossRef]
  16. Kumaresan, K.; Guo, O.; Ramada, P.; White, R.E. Cycle life performance of lithium-ion pouch cells. J. Power Sources 2006, 158, 679–688. [Google Scholar] [CrossRef]
  17. Abraham, D.P.; Liua, J.; Chen, C.H.; Hyung, Y.E.; Stolla, M.; Elsena, N.; MacLaren, S.; Twesten, R.; Haasch, R.; Sammann, E.; et al. Diagnosis of power fade mechanisms in high-power lithium-ion cells. J. Power Sources 2003, 119, 511–516. [Google Scholar] [CrossRef]
  18. Bodenes, L.; Dedryvere, R.; Martinez, H.; Fischer, F.; Tessier, C.; Peres, J.P. Lithium-ion batteries working at 85 °C: Aging phenomena and electrode/electrolyte interfaces studied by XPS. J. Electrochem. Soc. 2012, 159, 1739–1746. [Google Scholar] [CrossRef]
  19. Lee, S.; Pyun, S. The effect of electrolyte temperature on the passivity of the solid electrolyte interphase formed on a graphite. Carbon 2002, 40, 2333–2339. [Google Scholar] [CrossRef]
  20. Ning, G.; Haran, B.; Popov, B.N. Capacity fade of lithium ion batteries cycled at high discharge rates. J. Power Sources 2003, 117, 160–169. [Google Scholar] [CrossRef]
  21. Markovsky, B.; Rodkin, A.; Cohen, Y.S.; Palchik, O.; Levi, E.; Aurbach, D.; Kim, H.-J.; Schmidt, M. The study of capacity fading processes of Li-ion batteries: Major factors that play a role. J. Power Sources 2003, 119–121, 504–510. [Google Scholar] [CrossRef]
  22. Braithwaite, J.W.; Gonzales, A.; Nagasubramanian, G.; Lucero, S.J.; Peebles, D.E.; Ohlhausen, J.A.; Cieslak, W.R. Corrosion of lithium-ion battery current collectors. J. Electrochem. Soc. 1999, 146, 448–456. [Google Scholar] [CrossRef]
  23. Kim, J.S.; Park, Y.T. Characteristics of surface films formed at a mesocarbon microbead electrode in a Li-ion battery. J. Power Sources 2000, 91, 172–176. [Google Scholar] [CrossRef]
  24. Li, J.; Murphy, E.; Winnick, J.; Kohl, A.P. The effect of pulse charge on cycling characteristics of commercial lithium-ion batteries. J. Power Sources 2001, 102, 302–309. [Google Scholar] [CrossRef]
  25. Broussely, M.; Herreyre, S.; Biensan, P.; Kasztejna, P.; Nechev, K.; Staniewicz, R.J. Aging Mechanisms in Li ion cells and calendar life predictions. J. Power Sources 2001, 97, 13–21. [Google Scholar] [CrossRef]
  26. Li, J.; Murphy, E.; Winnick, J.; Kohl, P.A. Studies on the cycle life of commercial lithium ion batteries during the charge-discharge cycling. J. Power Sources 2001, 102, 294–301. [Google Scholar] [CrossRef]
  27. Aurbach, D.; Markovsky, B.; Talyossef, Y.; Salitra, G.; Kim, H.; Choi, S. Studies of cycling behaviour, ageing, and interfacial reactions of LiNi0.5Mn1.5O4 and carbon electrode for lithium-ion 5-V cells. J. Power Sources 2006, 162, 780–789. [Google Scholar] [CrossRef]
  28. Keun, C.; Yin, R.; Shin, S.; Lee, Y.; Choi, W.; Kim, Y. Electrochemical properties and gas evolution behavior of overlithiated Li2NiO2 as cathode active mass for rechargeable Li ion batteries. J. Electrochem. Soc. 2012, 159, 887–893. [Google Scholar] [CrossRef]
  29. Abraham, D.P.; Knuth, J.L.; Dees, D.W.; Bloom, I. Performance degradation of high power lithium ion cells- electrochemistry of harvested electrodes. J. Power Sources 2007, 170, 465–475. [Google Scholar] [CrossRef]
  30. Broussely, M.; Biensan, P.H.; Bonhomme, F.; Balnchard, P.H.; Herreyre, S.; Nechev, K.; Staniewicz, R.J. Main aging mechanisms in lithium ion batteries. J. Power Sources 2005, 146, 90–96. [Google Scholar] [CrossRef]
  31. Yamada, H.; Watanabe, Y.; Moriguchi, I.; Kudo, T. Rate capability of lithium intercalation into nano-porous graphitized carbon. Solid State Ionics 2008, 179, 1706–1709. [Google Scholar] [CrossRef]
  32. Fellner, J.P.; Loeber, G.J.; Sandhu, S.S. Testing of lithium-ion 18650 cells and characterizing/predicting cell performance. J. Power Sources 1999, 81, 867–871. [Google Scholar] [CrossRef]
  33. Smart, M.C.; Ratnakumar, B.V.; Surapudi, S.; Wang, Y.; Zhang, X.; Greenbaum, S.G.; Hightower, A.; Ahn, C.C.; Fultz, B. Irreversible capacities of graphite in low temperature electrolytes for lithium-ion batteries. J. Electrochem. Soc. 1999, 46, 3963–3969. [Google Scholar] [CrossRef]
  34. Moss, P.L.; Au, G.; Plichta, E.J.; Zheng, P.J. Study of capacity fade of lithium-ion polymer rechargeable batteries with continuous cycling. J. Electrochem. Soc. 2010, 157, A1–A7. [Google Scholar] [CrossRef]
  35. Wolfgang, M.; Lu, C.; Novak, P. Morphology of the solid electrolyte interphase of the graphite I dependency of the formation current. J. Electrochem. Soc. 2011, 1478–1482. [Google Scholar]
  36. Nakura, K.; Ohsugi, Y.; Imazaki, M.; Ariyoshi, K.; Ohzuku, T. Extended cycle life of lithium-ion batteries consisting of lithium insertion electrodes: cycle efficiency versus Ah efficiency. J. Electrochem. Soc. 2011, 158, 1243–1249. [Google Scholar] [CrossRef]
  37. Shim, J.; Striebel, K. Characterization of high-power lithium-ion cells during constant cycling: Part I cycling performance and electrochemical diagnostics. J. Power Sources 2003, 122, 188–194. [Google Scholar] [CrossRef]
  38. Shim, J.; Kostecki, R.; Richardson, T.; Song, X.; Striebel, K.A. Electrochemical analysis for cycle performance and capacity fading of a lithium-ion battery cycled at elevated temperature. J. Power Sources 2002, 112, 222–230. [Google Scholar] [CrossRef]
  39. Zhang, D.; Haran, B.S.; Durirajan, A.; White, R.E.; Podrazhansky, Y.M.; Popov, B.N. Studies on capacity fade of lithium-ion batteries. J. Power Sources 2000, 91, 122–129. [Google Scholar] [CrossRef]
  40. Kida, Y.; Kinoshita, A.; Yanagida, K.; Funahashi, A.; Nohma, T.; Yonezu, I. Study on capacity fade factors of lithium secondary batteries using LiNi0.7 Co0.3O2 and graphite-coke hybrid carbon. Electrochim. Acta 2002, 47, 4157–4162. [Google Scholar] [CrossRef]
  41. Utsunomiya, T.; Hatozaki, O.; Yoshimoto, N.; Egashira, M.; Morita, M. Influence of particle size on the self-discharge behavior of graphite electrodes in lithium-ion batteries. J. Power Sources 2011, 196, 8675–8682. [Google Scholar] [CrossRef]
  42. Wu, H.C.; Guo, Z.Z.; Wen, H.P.; Yang, M.Y. Study the fading mechanism of LiMn2O4 battery with spherical and flake type graphite as anode material. J. Power Sources 2005, 146, 736–740. [Google Scholar] [CrossRef]
  43. Sikha, G.; Ramadass, P.; Haran, B.S.; White, R.E.; Popov, B.N. Comparison of the capacity fade of Sony US 18650 cells charged with different protocols. J. Power Sources 2003, 122, 67–76. [Google Scholar] [CrossRef]
  44. Wang, C.; Appleby, A.J.; Little, F.E. Low-temperature characterization of lithium-ion carbon anodes via microperturbation measurement. J. Electrochem. Soc. 2002, 149, 754–760. [Google Scholar] [CrossRef]
  45. Zhang, Y.; Wang, C.Y. Cycle-life characterization of automotive lithium-ion batteries with LiNiO2. J. Electrochem. Soc. 2009, 156, 527–535. [Google Scholar] [CrossRef]
  46. Zhou, J.; Notten, P.H.L. Studies on degradation of Li-ion batteries by the use of micro reference electrodes. J. Power Sources 2008, 177, 553–560. [Google Scholar] [CrossRef]
  47. Jasen, N.A.; Dees, D.W.; Abraham, D.P.; Amine, K.; Henriksen, G.L. Low temperature study of lithium-ion cells using LiySn micro-reference electrode. J. Power Sources 2007, 174, 373–379. [Google Scholar] [CrossRef]
  48. Tsujikawa, T.; Yabuta, K.; Matsushita, T.; Arakawa, M.; Hayashi, K. A study on the cause of deterioration in float-charged lithium-ion batteries using LiMn2O4 as a cathode active material. J. Electrochem. Soc. 2011, 158, 322–325. [Google Scholar] [CrossRef]
  49. Sarre, G.; Balanchard, P.; Broussely, M. Aging of lithium-ion batteries. J. Power Sources 2004, 127, 65–71. [Google Scholar] [CrossRef]
  50. Brown, S.; Ogawa, K.; Kumeuchi, Y.; Enomoto, S.; Uno, M.; Saito, H.; Yoshisugu, S.; Abraham, D.; Lindberg, G. Cycle life evaluation of 3 Ah LixMn2O4-based lithium-ion secondary cells for low-earth-orbit satellites. J. Power Sources 2008, 185, 1444–1453. [Google Scholar] [CrossRef]
  51. Kostecki, R.; Lei, J.; McLarnon, F.; Shim, J.; Striebel, K. Diagnostic evaluation of detrimental phenomena in high-power lithium-ion batteries. J. Electrochem. Soc. 2006, 153, A669–A672. [Google Scholar] [CrossRef]
  52. Safari, M.; Delacourt, C. Aging of a commercial graphite LiFePO4 cell. J. Electrochem. Soc. 2011, 158, 1123–1135. [Google Scholar] [CrossRef]
  53. Sinha, N.N.; Smith, A.J.; Burns, J.C.; Gaurav, J.; Eberman, K.W.; Scott, E.; Gardner, J.P.; Dahn, J.R. The use of elevated temperature storage experiments to learn about parasitic reaction in wound LiCoO2/graphite cells. J. Electrochem. Soc. 2011, 158, 1194–1201. [Google Scholar] [CrossRef]
  54. Sinha, N.N.; Marks, T.H.; Dahn, H.M.; Smith, A.J.; Burn, J.C.; Coyle, D.J.; Dahn, J.J.; Dahn, J.R. The rate of active lithium loss from a soft carbon negative electrode as a function of temperature, time and electrode potential. J. Electrochem. Soc. 2012, 159, 1672–1681. [Google Scholar] [CrossRef]
  55. Novak, P.; Lanz, M.; Allia, D.; Rykart, B.; Paniz, J.; Haas, O. The complex electrochemistry of graphite electrodes in lithium-ion batteries. J. Power Sources 2001, 97, 39–46. [Google Scholar] [CrossRef]
  56. Wang, H.; Jang, Y.; Huang, B.; Sadoway, R.D.; Chiang, Y.M. TEM Study of Electrochemical Cycling-Induced Damage and Disorder in LiCoO2 Cathodes for Rechargeable Lithium Batteries. J. Electrochem. Soc. 1999, 146, 473–480. [Google Scholar] [CrossRef]
  57. Schranzhofer, H.; Bugajski, J.; Santner, H.J.; Korepp, C.; Moller, K.C.; Besenhard, J.O.; Winter, M.; Sitte, W. Electrochemical impedance spectroscopy study of the SEI formation on graphite and metal electrode. J. Power Sources 2006, 153, 391–395. [Google Scholar] [CrossRef]
  58. Markervich, E.; Salitra, G.; Levi, M.D.; Aurbach, D. Capacity fading of lithiated graphite electrodes studied by a combination of electroanalytical methods, Raman spectroscopy and SEM. J. Power Sources 2005, 146, 146–150. [Google Scholar] [CrossRef]
  59. Hossein, M.; Guoping, D.; Anaba, A.; Howard, J. Thermal Stability Studies of Li-Ion Cells and Components. J. Electrochem. Soc. 1999, 146, A3224–A3229. [Google Scholar] [CrossRef]
  60. Chang, Y.; Li, H.; Wu, L.; Lu, T. Irreversible capacity loss of graphite electrode in lithium-ion batteries. J. Power Sources 1997, 68, 187–190. [Google Scholar] [CrossRef]
  61. Shim, J.; Striebel, A.K. The dependence of natural graphite anode performance on electrode density. J. Power Sources 2004, 130, 247–253. [Google Scholar] [CrossRef]
  62. Lai, Y.; Cao, Z.; Haishen, S.; Zhang, Z.; Chen, X.; Lu, H.; Jia, M.; Li, J. Influence of Fe(II) species in electrolyte on performance of graphite anode for lithium-ion batteries. J. Electrochem. Soc. 2012, 159, 1961–1966. [Google Scholar] [CrossRef]
  63. Rhodes, K.; Kirkham, M.; Meisner, R.; Parish, M.C.; Dudney, N. Novel cell design for combined in situ acoustic emission and x-ray diffraction study during electrochemical cycling of batteries. Rev. Sci. Instrum. 2011, 82, 75–107. [Google Scholar]
  64. Nagpure, S.C.; Bhushan, B.; Babu, S.; Rizzoni, G. Scanning spreading resistance characterization of aged Li-ion batteries using atomic force microscopy. Scripta Mater. 2009, 60, 933–936. [Google Scholar] [CrossRef]
  65. Ohzuku, T.; Ueda, A.; Yamamoto, N.; Yasunobu, I. Factor affecting the capacity retention of lithium-ion cells. J. Power Sources 1995, 54, 99–102. [Google Scholar] [CrossRef]
  66. Jeong, S.K.; Inaba, M.; Takeshi, A.; Ogumi, Z. Surface film formation on graphite negative electrode in lithium-ion batteries. J. Electrochem. Soc. 2001, 148, A989–A993. [Google Scholar] [CrossRef]
  67. Silvakkumar, S.R.; Nerkar, J.Y. Rate capability of graphite materials as negative electrodes in lithium ion capacitors. Electrochim. Acta 2010, 55, 3330–3335. [Google Scholar] [CrossRef]
  68. Simon, B.; Flandrois, S.; Guerin, K.; Ferrier-Bouvier, A.; Teulat, I.; Biensan, P. On the choice of graphite for lithium ion batteries. J. Power Sources 1999, 81, 312–316. [Google Scholar] [CrossRef]
  69. Ridgway, P.; Zheng, H.; Bello, A.F.; Song, X.; Xun, S.; Chong, J.; Vincent, B. Comparison of cycling performance of lithium ion cell anode graphites. J. Electrochem. Soc. 2012, 159, 520–524. [Google Scholar] [CrossRef]
  70. Anderson, A.M.; Edstrom, K.; Thomas, J.O. Characterization of the ambient and elevated temperature performance of graphite electrode. J. Power Sources 1999, 81–82, 8–12. [Google Scholar] [CrossRef]
  71. Tran, T.D.; Feikert, J.H.; Pekala, R.W. Rate effect on lithium-ion graphite electrode performance. J. Appl. Electrochem. 1996, 26, 1161–1167. [Google Scholar] [CrossRef]
  72. Park, Y.; Lee, S. Effect of particle size on the thermal stability of lithiated graphite. Electrochim. Acta 2009, 54, 3339–3343. [Google Scholar] [CrossRef]
  73. Nga, S.H.; Vix-Guterl, C.; Bernardo, P.H.; Tran, N.; Ufheil, J.; Buqa, H.; Dentzer, J.; Gadiou, R.; Spahr, M.E.; Goers, D.; et al. Correlations between surface properties of graphite and the first cycle specific charge loss in lithium-ion batteries. Carbon 2009, 47, 705–712. [Google Scholar] [CrossRef]
  74. Joho, F.; Rykart, B.; Wilhem, H.; Novak, P.; Spahr, M.E.; Monnier, A. Relation between surface properties, pore structure and first cycle charge loss of graphite as negative electrode in lithium-ion batteries. J. Power Sources 2001, 97, 78–82. [Google Scholar] [CrossRef]
  75. Aurbach, D.; Teller, H.; Koltypin, M.; Levi, E. On the behaviour of different types of graphite anodes. J. Power Sources 2003, 119–121, 2–7. [Google Scholar] [CrossRef]
  76. Wu, Q.; Lu, W.; Prakash, J. Charaterization of commercial size cylindrical Li-ion cell with a reference electrode. J. Power Sources 2000, 88, 237–242. [Google Scholar] [CrossRef]
  77. Rubino, S.R.; Gan, H.; Takeuchi, S.E. A study of capacity fades in cylindrical and prismatic lithium-ion batteries. J. Electrochem. Soc. 2001, 148, 1029–1033. [Google Scholar] [CrossRef]
  78. Shim, J.; Striebel, A.K. Effect of electrode density on cycle performance and irreversible capacity loss for natural graphite anode in lithium-ion batteries. J. Power Sources 2003, 119, 934–937. [Google Scholar] [CrossRef]
  79. Leising, A.R.; Palazzo, M.J.; Takeuchi, S.E.; Takeuchi, J.K. Abuse Testing of Lithium-Ion Batteries Characterization of the Overcharge Reaction of LiCoO2/Graphite Cells. J. Electrochem. Soc. 2001, 148, 838–844. [Google Scholar] [CrossRef]
  80. Lanz, M.; Novak, P. DEMS study of gas evolution at thick graphite electrodes for lithium-ion batteries: The effect of the γ-butyrolactone. J. Power Sources 2001, 102, 277–282. [Google Scholar] [CrossRef]
  81. Ratnakumar, B.V.; Smart, M.C. Lithium plating behavior in lithium-ion cells. J. Electrochem. Soc. Trans. 2010, 25, 241–252. [Google Scholar]
  82. Dolle, M.; Sannier, L.; Beaudion, B.; Trentin, M. Live scanning electron microscope observation of dendrite growth in lithium polymer cells. J. Electrochem. Soc. 2002, 5, 286–289. [Google Scholar]
  83. Smart, M.C.; Ratnakumar, B.V. Effects of electrolyte composition on lithium plating in lithium-ion cells. J. Electrochem. Soc. 2011, 158, 379–389. [Google Scholar] [CrossRef]
  84. Honbo, H.; Takei, K.; Ishii, Y.; Nishida, T. Electrochemical properties and Li deposition morphologies of surface modified graphite after grinding. J. Power Sources 2009, 189, 337–343. [Google Scholar] [CrossRef]
  85. Rosso, M.; Gobron, T.; Brissot, C.; Chazalviel, J.N.; Lascaud, S. Onset of dendritic growth in lithium/polymer cells. J. Power Sources 2001, 97, 804–806. [Google Scholar] [CrossRef]
  86. Ornini, F.; Pasquier, D.A.; Beaudion, B.; Tarason, J.M.; Trentin, M. In situ scanning electron microscope observation of interfaces within plastic lithium batteries. J. Power Sources 1998, 76, 19–29. [Google Scholar] [CrossRef]
  87. Leising, R.A.; Palazzo, M.J.; Takeuchi, E.S.; Takeuchi, K.J. A study of the overcharge reaction of lithium-ion batteries. J. Power Sources 2001, 97, 681–683. [Google Scholar] [CrossRef]
  88. Kim, W.; Yoon, W. Observation of dendritic growth on Li powder anode using the optical cell. Electrochim. Acta 2004, 50, 541–545. [Google Scholar] [CrossRef]
  89. Kong, S.; Kim, B.; Yoon, W. Electrochemical behavior of Li-powder anode in high Li capacity used. J. Electrochem. Soc. 2012, 159, 1551–1553. [Google Scholar] [CrossRef]
  90. Bhattacharyya, R.; Key, B.; Chen, H.; Best, A.S.; Hollenkamp, A.F.; Grey, C.P. In situ NMR observation of the formation of metallic microstructure in lithium batteries. Nat. Mater. 2010, 9, 504–510. [Google Scholar]
  91. Lu, W.; Carmen, M.; Liu, N.; Vaughely, T.J.; Jansen, A.; Dees, D.W. Overcharge effect on morphology and structure of carbon electrodes for lithium-ion batteries. J. Electrochem. Soc. 2012, 159, 566–570. [Google Scholar] [CrossRef]
  92. Fan, J.; Tan, S. Studies on charging lithium-ion cells at low temperatures. J. Electrochem. Soc. 2006, 153, 1081–1092. [Google Scholar] [CrossRef]
  93. Joho, F.; Rykart, B.; Imhof, R.; Novak, P.; Spahr, M.E.; Monnier, A. Key factors for the cycling stability of graphite intercalation electrodes for lithium-ion batteries. J. Power Sources 1999, 81, 243–247. [Google Scholar] [CrossRef]
  94. Park, Y.; Bang, H.J.; Oh, S.; Sun, Y.; Lee, S. Effect of carbon coating on thermal stability of natural graphite spheres used as anode materials in lithium-ion batteries. J. Power Sources 2009, 190, 553–557. [Google Scholar] [CrossRef]
  95. Chevsllier, F.; Gautier, S.; Salvetat, J.P.; Clinard, C.; Frackowiak, E.; Rouzaud, J.N.; Beguin, F. Effects of post-treatment on performance of hard carbons in lithium cells. J. Power Sources 2001, 97, 143–145. [Google Scholar]
  96. Natarajan, C.; Fujimoto, H.; Tokumitsu, K.; Mabuchi, A.; Kasuh, T. Reduction of irreversible capacity of a graphite anode by the CVD process. Carbon 2001, 39, 1409–1413. [Google Scholar] [CrossRef]
  97. Striebel, K.A.; Sierra, A.; Shim, J.; Wang, C.W.; Saatry, A.M. The effect of compression on natural graphite anode performance and matrix conductivity. J. Power Sources 2004, 234, 241–251. [Google Scholar] [CrossRef]
  98. Shim, J.; Striebel, K.A. Electrochemical characterization of thermally oxidized natural graphite anodes in lithium-ion batteries. J. Power Sources 2007, 164, 862–867. [Google Scholar] [CrossRef]
  99. Choi, S.S.; Lim, H.S. Factors that affect cycle life and possible degradation mechanisms of a Li-ion cell based on LiCoO2. J. Power Sources 2002, 111, 130–136. [Google Scholar] [CrossRef]
  100. Nobili, F.; Mancini, M.; Dsoke, S.; Tossici, R.; Marassi, R. Low-temperature behavior of graphite–tin composite anodes for Li-ion batteries. J. Power Sources 2010, 195, 7090–7097. [Google Scholar] [CrossRef]
  101. Rubino, R.S.; Takeuchi, S.E. The study of irreversible capacity in lithium-ion anodes prepared with thermally oxidized graphite. J. Power Sources 1999, 81, 373–377. [Google Scholar] [CrossRef]

Share and Cite

MDPI and ACS Style

Agubra, V.; Fergus, J. Lithium Ion Battery Anode Aging Mechanisms. Materials 2013, 6, 1310-1325. https://doi.org/10.3390/ma6041310

AMA Style

Agubra V, Fergus J. Lithium Ion Battery Anode Aging Mechanisms. Materials. 2013; 6(4):1310-1325. https://doi.org/10.3390/ma6041310

Chicago/Turabian Style

Agubra, Victor, and Jeffrey Fergus. 2013. "Lithium Ion Battery Anode Aging Mechanisms" Materials 6, no. 4: 1310-1325. https://doi.org/10.3390/ma6041310

Article Metrics

Back to TopTop