-
During overcharging of lithium-ion batteries, lithium plating can occur on the anode surface when the maximum lithium intercalation concentration is exceeded, while the cathode is in a lithium-poor state, which can result in shortened battery lifespan and safety. In this work, the geometric structure of the positive electrode particles is designed based on the tomography data, while the negative electrode particles are represented by spheres with different sizes. The homogenization method is used, with the carbon filler, binder and electrolyte regarded as a single porous conductive adhesive domain. Based on the main mechanism of lithium-ion battery overcharge, a coupled three-dimensional electrochemical-mechanical-thermal overcharge model on a particle scale is developed for NCM cathode and graphite anode. The coupled mathematical model consists of four parts, namely the electrochemical model, the lithium plating model, the thermal model and the stress-strain model. In terms of lithium precipitation, the particle radius parameter and charging rates are investigated. The results show that the lithium plating concentration of the particles near the separator is higher, following the “principle of proximity” , namely the sequence of lithium deintercalation is related to the migration path. The surface of anode particles with small particle size is more prone to lithium precipitation due to the high maximum lithium ion concentration on the surface of the particles, the low surface lithium precipitation overpotential, and the high average Von Mises stress. At high charging rate, fast charge transfer rate and ion diffusion rate result in a low voltage at the anode, triggering off lithium precipitation. At a low rate, polarization and low temperature can lead to the precipitation of more lithium on the surface of the anode particles. In terms of stress, the spatial distribution between particles and thermal effects are investigated. The ratio of the distance from the contact surface to the center of the particle to the particle radius is calculated and defined as the contact depth ($Jr$), in order to better describe the law of particle contact stress. It is shown that the contact depth between particles is inversely proportional to the stress on the contact area. When the heat generation effect is considered, the temperature of the battery rises faster with the increase of the charging rate. The electrochemical parameters related to temperature and the lithium concentration diffusion gradient increase significantly, and the influence of temperature on the particle stress is also more significant. The relevant results can provide theoretical basis and guidance for designing battery and optimizing charge strategies.
-
图 1 模型几何图和耦合关系图 (a) 几何模型; (b) 网格; (c) 数学模型之间的耦合关系
Figure 1. Geometric shape and coupling relationship diagram of the model: (a) Geometric shape; (b) mesh; (c) coupling relationship between mathematical models.
图 4 电压的仿真数据与实验数据的对比 (a) 充电至4.2 V时, 充电倍率为0.2C, 0.5C, 1C和1.5C的电压变化图; (b) 充电至4.8 V时, 充电倍率为0.2C, 0.5C的电压变化图
Figure 4. Comparison between simulated and experimental data of voltage: (a) Voltage variation graphs charging to 4.2 V at charging rates of 0.2C, 0.5C, 1C and 1.5C; (b) voltage variation graphs charging to 4.8 V at charging rates of 0.2C and 0.5C.
图 5 (a) 负极颗粒表面析出锂金属浓度分布; (b) 负极颗粒表面析锂过电位绝对值分布; (c) 不同粒径颗粒位置示意(蓝色标记)
Figure 5. (a) Lithium metal concentration on the particle surface; (b) the absolute value of overpotential of lithium plating on the particle surface; (c) position of particles with different sizes (the blue area).
图 6 在负极两个颗粒表面的过充过程 (a) 析出锂金属浓度; (b) 最大锂离子浓度; (c) 平均析锂过电位; (d) 平均冯·米塞斯应力
Figure 6. Overcharging process on the surfaces of two negative particles: (a) Concentration of lithium metal precipitated; (b) maximum lithium ion concentration; (c) average lithium precipitation overpotential; (d) average von Mises stress.
图 7 不同倍率下的负极整个表面析出的锂金属浓度(a)和负极颗粒的温度(b)
Figure 7. (a) Lithium metal concentration precipitated on the whole surface of the negative electrode and (b) the temperature of the negative electrode particles at different charging rates.
图 8 (a) 0.5C充电至4.8 V的正极应力-应变; (b) 0.5C充电至4.8 V的正极与负极应力
Figure 8. (a) Stress-strain of the cathode charged to 4.8 V at 0.5C; (b) stress of the cathode and anode charged to 4.8 V at 0.5C.
图 9 0.5C充电至3.9 V, 4.2 V, 4.5 V, 4.8 V的正极颗粒应力-应变分布图
Figure 9. Stress-strain distribution diagrams of cathode particles charged to 3.9 V, 4.2 V, 4.5 V and 4.8 V at 0.5C.
图 10 A, B, C和D四组颗粒的接触应力-应变(a)和位置(b)
Figure 10. (a) Contact stress and strain of particles and (b) corresponding position in groups A, B, C and D.
图 11 0.2C (a), (c) 和0.5C (b), (d)倍率下, 正极颗粒平均冯·米塞斯应力, 以及温度相关系数随充电过程变化
Figure 11. Average von Mises stress of positive electrode particles and temperature-dependent coefficient at 0.2C (a), (c) 和0.5C (b), (d).
表 1 电化学过充模型中的几何参数和结构
Table 1. Geometric parameters and structure of the electrochemical overcharge model.
参数 负极 隔膜 正极 长度L/μm 80 30 95 颗粒平均半径Rs_avg/μm 4.15 — 6.19 颗粒最大/最小半径Rsmax/min/μm 14.61/1.03 — 14.25/1.62 颗粒面积Ap/μm2 24997 — 20553 颗粒体积Vp/μm3 37892 — 36193 电池截面长度Lcross/μm 37 电池截面宽度Across/μm2 34.4 比表面积av/m–1 2.52×105 — 1.69×105 固相体积分数ψs 0.3833 — 0.2984 液相体积分数ψe 0.6167 — 0.7015 
DownLoad: CSV
参数 负极 隔膜 正极 密度ρ/kg·m3 2300 1000 4530 杨氏模量E/ GPa 1047 78 泊松比nu 0.3 0.25 热膨胀系数αT/K–1 4.06×10–6 1.2×10–5 电池比热容Cp/(J·kg–1·K–1) 881 1260 1009.21 对流系数h/(W·m–2·K–1) 10
DownLoad: CSV
参数 负极 隔膜 正极 固相电子电导率σs/(S·m–1) 100 — 3.8 固相有效电子电导率σs, eff/(S·m–1) ψs1.5σs ψs1.5σs 液相离子电导率σe/(S·m–1) ce(5.38-3.49×10–4ce+2.3×10–7ce2)2×10–4 液相有效离子电导率σe, eff/(S·m–1) ψe1.5σe 液相电子电导率σca/(S·m–1) 10 σe的活性能Ea, σe/(kJ·mol–1) 30 初始电解质浓度ce, 0/(mol·m–3) 1200 最大固相锂浓度cs, max/(mol·m–3) 24407 — 30017 化学计量系数x在1/0 SOC 0.115/0.98 — 0.92/0.222 容量比N/P 1.09 固相扩散系数Ds/(m2·S–1) 1.45×10–13 — 2×10–13 液相扩散系数De/(m2·S–1) $ {10^{[ - 8.43 - 54/(59.15 - 0.05{c_{\text{e}}}}}^{) - 2.2 \times {{10}^{ - 4 c_{\text{e}}^2}}]} $ 液相有效扩散系数De, eff/(m2·S–1) ψe1.5De De的活化能Ea, De/(kJ·mol–1) 72
DownLoad: CSV
参数 负极 隔膜 正极 反应的传递系数αa, 1, αc, 1 0.5, 0.5 0.5, 0.5 反应速率常数k1, ref/(m·s–1) 2×10–11 2×10–11 k1的活化能Ea, k1/(kJ·mol–1) 71 45 析锂反应传递系数αa, 2, αc, 2 0.3, 0.7 析锂反应速率常数k2, ref/(m·s–1) 2.5×10–7 k2的活化能Ea, k2/(kJ·mol–1) 50 锂的摩尔质量Mpl/(kg·mol–1) 6.94×10–5 锂的密度ρpl/(kg·m–3) 534 电导率σfilm/(S·m–1) 6×10–5 析锂的平衡电位Eeq, Li/V 0
DownLoad: CSV
-
[1] Yong J Y, Ramachandaramurthy V K, Tan K M, Mithulananthan N 2015 Renew. Sust. Energ. Rev. 49 365
Google Scholar
[2] Crabtree G 2019 Science 366 422
Google Scholar
[3] Huang W S, Feng X N, Han X B, Zhang W F, Jiang F C 2021 Cell Rep. Phys. Sci. 2 100285
Google Scholar
[4] Wang Q S, Mao B B, Stoliarov S I, Sun J H 2019 Prog. Energ. Combust. 73 95
Google Scholar
[5] Belova I V, Murch G E 1995 J. Appl. Phys. 77 127
Google Scholar
[6] Zhao Y, Stein P, Bai Y, Al-Siraj M, Yang Y Y W, Xu B X 2019 J. Power Sources 413 259
Google Scholar
[7] Pastor-Fernández C, Uddin K, Chouchelamane G H, Widanage W D, Marco J 2017 J. Power Sources 360 301
Google Scholar
[8] 王其钰, 王朔, 周格, 张杰男, 郑杰允, 禹习谦, 李泓 2018 物理学报 67 128501
Google Scholar
Wang Q Y, Wang S, Zhou G, Zhang J N, Zhen J Y, Yu X Q, Li H 2018 Acta Phys. Sin. 67 128501
Google Scholar
[9] Honbo H, Takei K, Ishii Y, Nishida T 2009 J. Power Sources 189 337
Google Scholar
[10] Mei W X, Duan Q L, Qin P, Xu J J, Wang Q S, Sun J H 2019 J. Electrochem. Soc. 166 A3319
Google Scholar
[11] Arora P, Doyle M, White R E 1999 J. Electrochem. Soc. 146 3543
Google Scholar
[12] Ren D S, Smith K, Guo D X, Han X B, Feng X N, Lu L G, Ouyang M G, Li J Q 2018 J. Electrochem. Soc. 165 A2167
Google Scholar
[13] Mei W X, Zhang L, Sun J H, Wang Q S 2020 Energy Storage Mater. 32 91
Google Scholar
[14] Yang S, Hua Y, Qiao D, Lian Y, Pan Y, He Y 2019 Electrochim. Acta 326 134928
Google Scholar
[15] Wang Y N, Li H, Wang Z K, Lian C, Xie Z F 2021 J. Energy Storage 43 103214
Google Scholar
[16] Schmidt A, Ramani E, Carraro T, Joos J, Weber A, Kamlah M, Ivers-Tiffée E 2021 Energy Technology 6 2000881
[17] Ebner M, Geldmacher F, Marone F, Stampanoni M, Wood V 2013 Adv. Energ. Mater. 3 845
Google Scholar
[18] 李涛, 程夕明, 胡晨华 2021 物理学报 70 138801
Google Scholar
Li T, Cheng X M, Hu C H, 2021 Acta Phys. Sin. 70 138801
Google Scholar
[19] Yang F Q 2016 Sci. China Phys. Mech. 59 44
[20] Newman J S, Tobias C W 1962 J. Electrochem. Soc. 109 1183
Google Scholar
[21] Ge H, Aoki T, Ikeda N, Suga S, Isobe T, Li Z, Tabuchi Y, Zhang J 2017 J. Electrochem. Soc. 164 A1050
Google Scholar
[22] David W I F, Thackeray M M, De Picciotto L A, Goodenough J B 1987 J. Solid State Chem. 67 316
Google Scholar
[23] Yang F 2005 Mater. Sci. Eng. A 409 153
Google Scholar
[24] Wu B, Lu W 2017 J. Power Sources 360 360
Google Scholar
[25] Guo M, Sikha G 2010 J. Electrochem. Soc. 158 A122
[26] 蒋跃辉, 艾亮, 贾明, 程昀, 杜双龙, 李书国 2017 物理学报 66 118202
Google Scholar
Jang Y H, Ai L, Jia M, Cheng J, Du S L, Li S G 2017 Acta Phys. Sin. 66 118202
Google Scholar
[27] Wu W, Xiao X, Huang X, Yan S 2014 Comp. Mater. Sci. 83 127
Google Scholar
[28] Samba A, Omar N, Gualous H, Capron O, Van B P, Van M J 2014 Electrochim. Acta 147 319
Google Scholar
[29] Lai Y, Du S, Ai L, Cheng Y, Tang Y, Jia M 2015 International Journal of Hydrogen Energy 40 13039
Google Scholar
[30] Mei W X, Chen H, Sun J H, Wang Q S 2018 Appl. Therm. Eng. 142 148
Google Scholar
[31] Hahn M, Buqa H, Ruch P W, Goers D, Spahr M E, Ufheil J, Novák P, Kötz R 2008 Electrochem. Solid State Lett. 11 A151
Google Scholar
[32] Kondrakov A O, Schmidt A, Xu J, Geßwein H, Mönig R, Hartmann P, Sommer H, Brezesinski T, Janek J 2017 J. Phys. Chem. C 121 3286
Google Scholar
[33] Hosseinzadeh E, Genieser R, Worwood D, Barai A, Marco J, Jennings P 2018 J. Power Sources 382 77
Google Scholar
[34] Yang Y, Zhong X L, Xu L 2024 J. Energy Chem. 97 453
Google Scholar
[35] 魏振伟, 毛烁源, 汪宇, 韩雪冰, 卢兰光, 欧阳明高 2024 上海理工大学学报 46 1
Wei Z W, Mao L Y, Wang Y, Lu L G, Ouyang M G 2024 J. Univ. Shanghai Sci. Tech. 46 1
[36] Mao S, Wang Y, Lu Y 2024 InfoMat e12612
[37] Wu W, Ma R, Liu J, Liu M, Wang We, Wang Q 2021 Int. J. Heat Mass Tran. 170 121024
Google Scholar
[38] Luo C X, Shi C G, Yu Z Y, Huang L, Sun S G 2022 J. Electrochem. 28 7
[39] Manthiram A 2020 Nat. Commun. 11 1550
Google Scholar
DownLoad:
Metrics
- Abstract views: 255
- PDF Downloads: 5
- Cited By: 0
