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SN Applied Sciences

, 1:205 | Cite as

Effects of gelation behavior of PPC-based electrolyte on electrochemical performance of solid state lithium battery

  • Te-te He
  • Mao-xiang JingEmail author
  • Hua Yang
  • Hao Chen
  • Song Hua
  • Bo-wei Ju
  • Qian Zhou
  • Fei-yue Tu
  • Xiang-qian Shen
  • Shi-biao QinEmail author
Research Article
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Part of the following topical collections:
  1. 4. Materials (general)

Abstract

Polypropylene carbonate (PPC)-based solid state electrolyte was fabricated by using a cellulose membrane as a skeleton. The gelation behavior of the PPC-based solid electrolytes in solid-state lithium batteries was found, and the effect of this behavior on battery performance was studied. It was found that the solute lithium salt in the matrix greatly promoted the gelation of the PPC-based solid electrolyte under heating conditions upon contact with metallic lithium. This behavior allows the room temperature conductivity of the electrolyte to be directly increased by two orders of magnitude, on the order of 10−3 S/cm, and also greatly improves the wettability of the electrode interface. The mechanism of in situ gelation allows the solid state battery to actually operate in a gel state. Since the actual electrochemical window of the electrolyte is only 3.8 V due to gelation, the electrolyte membrane continuously undergoes side reactions during the high voltage cycle, resulting in a continuous decrease in cycle efficiency.

Keywords

PPC-based electrolyte Gelation behavior Solid state battery Ionic conductivity 

1 Introduction

Solid electrolyte (SE) is the core of research in all-solid-state battery technology. The current mainstream SE includes the solid inorganic electrolyte and the solid polymer electrolyte (SPE). The former is mainly divided into two major directions of oxides and sulfides; the latter mainly includes polyethylene oxide (PEO), polycarbonate (PC) and the like. For SPE, although the RT ionic conductivity and stability are not as good as inorganic substances, it has great advantages in comprehensive electrochemical performance and preparation, such as: good interface wetting, flexible film preparation process, acceptable ion migration number and electrochemical window [1, 2, 3, 4, 5, 6, 7, 8, 9]. In fact, good interfacial wetting and simple thin film process are unique advantages of SPE [10, 11].

Compared with the most studied PEO solid electrolytes [8], PC-based solid electrolytes have obvious advantages [6, 7, 12, 13, 14, 15, 16, 17, 18, 19]: (1) RT conductivity can reach 10−4 S cm−1 or more; (2) The electrochemical window can reach more than 4 V; (3) The ion migration number can reach 0.5 or more. These advantages are the focus of the electrochemical performance of SPE. Cui made a comprehensive study on PC-based solid electrolytes, and proposed the concept of “rigid and flexible” to improve the mechanical strength of polymer matrix and obtained all solid state cell with long cycle stability [6, 13, 18]. Tominaga obtained a solid electrolyte membrane with the electrochemical window of 5 V and ion migration number of more than 0.5 by studying the polyethylene carbonate (PEC) solid electrolyte, and the RT conductivity reached 10−5 S cm−1 at a lithium salt addition of 188 mol%, metal lithium cell matching LiFePO4 positive electrode had excellent rate performance [20]. All of the above work shows that PC-based SPEs have great application prospects.

What’s the main reason for PC-based SPEs have so many excellent RT characteristics different from conventional SPEs? In our work, we prepared PPC-based solid electrolyte and studied the reaction process in solid state battery, found that a gelation process could be occurred when PPC was in contact with metallic lithium, which greatly influenced the electrochemical performances of the solid state battery.

1.1 Material preparation

In order to improve the mechanical strength of the PPC solid film, a commercial cellulose membrane was used as a support skeleton for the PPC solid film [13, 18, 19]. The entire preparation process was shown in Fig. 1: First, 5 g PPC was sufficiently dissolved with 10 g N,N-dimethylformamide (DMF), followed by addition of a certain amount of LITFSI, and then the mixture was thoroughly stirred to obtain a premix. A 100 μm thick premix was scraped on the steel plate, then a porous cellulose film was laid, and a slurry having a thickness of 400 μm was scraped off, finally dried in a vacuum oven at 100 °C for 24 h, peeled off to obtain the PPC-based SPE supported by a skeleton (CPPC-SPE). The similar preparation process was used to prepare a PPC-based SPE without skeleton (PPC-SPE) and without lithium salt (PPC). The thickness of the electrolyte membrane prepared above was 100 ± 5 μm.
Fig. 1

Preparation process of PPC-based solid electrolyte membrane

2 Electrochemical performance

2.1 RT conductivity of dry film

Unlike the PEO, PPC is a glassy state with high hardness at room temperature [14, 24]. so if simply using the conventional method, assembling the of “SS (stainless steel)/SPE/SS” structure (SS symmetrical cell) blocking ion migration for measuring the impedance of the SPE may cause the testing error of the SPE to be excessive due to the poor contact of the SS/membrane interface [6, 7, 21]. Therefore, in this experiment, the “soldering” of the SS/membrane interface was carried out using a polar solvent, so that the interface contact of the blocking electrode was greatly improved, and the conductivity obtained by the test was in accordance with expectations [6, 14, 15]. It can be seen from the Fig. 2, that the RT conductivity of the CPPC-SPE reaches the maximum, which is 4.3 × 10−5 S cm−1 when the amount of lithium salt added is 30%. So we choose 30% as the lithium salt content of the following SPE unless otherwise specified.
Fig. 2

Ionic conductivity of CPPC-SPE in RT before gelation

2.2 Ion migration number and electrochemical window

A metal lithium symmetrical cell “Li/CPPC-SPE/Li” was assembled to directly test the ion migration number of the CPPC-SPE. However, it was found during the test that the open circuit voltage (OCV) of the cell was extremely unstable and the DC bias could not be applied correctly. We compared the OCV of the “SS/CPPC-SPE/Li” (called “LSV cell”) and found the same phenomenon, as shown in the Fig. 3b, it is also impossible to test its electrochemical window [6, 7, 9, 16, 20]. Corresponding to the SS symmetrical cell that was not processed before, the unstable OCV should be caused by the poor interface contact.
Fig. 3

a OCV voltage of the unheated lithium symmetrical cell; b OCV voltage of the LSV cell; c polarization curve and corresponding impedance spectrum of the lithium symmetrical cell after heating; d step voltage-current curve of LSV cell

In order to prove the conjecture above, all the cells at 100 °C for 12 h before testing. After that, we found that the OCV of the symmetrical cells are stable other than “SS symmetrical cell”. The impedance spectrum and polarization curve obtained by the test are shown in the Fig. 3c. It has been calculated that the ion migration number is 0.49, which is more than twice that of PEO-SPE [8]. The polarization curve of the LSV cell was successfully obtained, shown in the Fig. 3d. The electrochemical window of CPPC-SPE reached to 4.6 V, which was close to the literature [6, 13].

So what happened inside PPC-based SPE cell during heating so as to get the normal results? We conducted follow-up experiments.

3 Gelation of CPPC-SPE

3.1 Scanning electron micrograph

A lithium symmetrical cell was assembled with CPPC-SPE to observe the change of CPPC-SPE in contact with metallic lithium under different conditions. The surface of the CPPC-SPE not in contact with metallic lithium is shown in Fig. 4a, and the surface is smooth. However, after heating, as is shown in Fig. 4b, the surface skeleton of the film is exposed to a serious extent, and only a small part of the voids are filled with a certain amount of polymer along with some obvious liquid. It demonstrates that CPPC-SPE will gel after heated when in contact with the metal lithium [21]. To further illustrate the problem, PPC-SPE under the same conditions was applied, and it was found that the membrane “disappears” after heating, in the meanwhile, a certain amount of liquid generated while the membrane still existed and hardly changed in the unheated one.
Fig. 4

a Unheated film surface photo ×2000; b heated SEM photo ×2000; c partially magnified SEM photograph ×10,000 in red frame of b; d digital photo of pure PPC after heated; e digital photo of PPC-SPE after heated

Both two experiments can show the fact that: (1) Heating can lead to gelation of the CPPC-SPE; (2) when there is no backbone support, the polymer will completely liquefy. Therefore, the skeleton plays an important role in the PPC-based solid metal lithium cell. So how does the gelation occur during the heating process?

3.2 Short circuit test

In order to characterize the detail of the CPPC-SPE gelation process during heating, lithium symmetrical cell assembled with PPC-SPE was applied. Electrochemical workstation was used to perform constant current charge and discharge at 100 °C to observe the polarization voltage. It was charged—1 h followed by discharged—1 h with the current of 0.5 mA. The polarization voltage reflected the change of the PPC-SPE inside cell.

At the beginning of the first charge, the polarization voltage was as high as 16.8 V, which made it possible to calculate an interface impedance of up to 16,750 Ω [22, 23, 24]. When 1085 s, the polarization voltage suddenly dropped. It cost 47 s from 16.8 V to 1 V, then dropped to 8 mV after 2028 s, and the interface impedance was only 6 Ω, the cell being circuit obviously. The interface impedance varied from 16,750 Ω to 6 Ω, indicating that the polymer matrix had begun to gel rapidly during the time, which greatly improved the wettability of the electrode interface. And after quickly dropped, the polarization voltage was slowly close to 0 mV whatever charge or discharge due to the slowly increasing wettability of the interface. After the test completed, the cell impedance was further tested. The impedance spectrum shown in the Fig. 5b also proves the cell short-circuited. In combination with the state of gelation of the heated PPC film concluded from the change of polarization voltage, it can be inferred that in the operation of the circulating cell, if there is no skeleton as the separation layer, it is likely to be thoroughly short-circuited after the cell is heated about 3160 s.
Fig. 5

a Constant current charge and discharge curve; b impedance spectrum after charge and discharge

The fact indicates that the cellulose film skeleton is necessary, not only to improve the mechanical strength, more importantly for physically separating, that is, when the PPC gels to “disappear”, it acts as a separator to prevent short circuit [21].

4 The cause of gelation

4.1 Analysis of the cause of PPC gelation

In order to find out the cause of PPC gelation, we assembled a cell with different electrode matching, and the structure was “electrode 1/CPPC-SPE/electrode 2”. As shown in Table 1, under different conditions, we used “Yes” or “No” to indicate whether the corresponding phenomenon occurred.
Table 1

Electrolyte film state under different electrode matching

LITFSI content

30% LITFSI

Free

Lithium symmetrical

Phenomenon

Type of cell

NCM523 symmetrical

SS symmetrical

Lithium symmetrical

LSV Cell

Heated or not?

√ (Yes)

× (No)

×

×

×

×

Dry or not?

×

×

×

Can getting impedance spectrum?

×

×

×

×

×

×

×

×

The phenomenons of the above control experiments show that: (1) only when exposed to metallic lithium, the film can appear liquid; (2) if the SPE is dry, the impedance spectrum cannot be obtained, indicating that the interface impedance is extremely large or unstable; (3) the addition of lithium salt and heating is necessary for ensuring the liquid generates when SPE is in contact with the metallic lithium. In fact, the liquid also appeares when CPPC-SPE in contact with Li(OH)2 [25], indicating that the trace of Li(OH)2 impurity on the surface of the metallic lithium also causes CPPC-SPE gelation [21].

Based on the above analysis, we can make the following speculation: the reason that the metal lithium solid state cell assembled by the PPC-based electrolyte can circulate well is the positive and negative electrodes infiltrated well due to the gelation of PPC. It also indicates that probably the PPC-based solid electrolyte membrane is not suitable for graphite or silicon carbon anode because of high interface impedance without gelation.

4.2 PPC gelation product analysis

In order to determine the product after PPC degradation, we used Fourier transform infrared spectroscopy to analyze the characteristic groups of the electrolyte membrane under different conditions. The results were shown in Fig. 6. Lithium ions form complexes with ester groups of PPC [13]. The anion and anion of lithium salts exist in the form of free ions, ion pairs and aggregates. These existences make the segment and chemical bond of PPC unstable. Under heating conditions, the segmental structure of PPC gels to form small molecular segments [21].
Fig. 6

Fourier infrared spectroscopy of CPPC-SPE under different conditions

Comparing the 30% lithium salt CPPC-SPE before and after heating, it is found that the characteristic spectrum of PC appeared in the heated state. Heating promotes the breakage of the ester group and produces PC, and a small amount of hydroxyl-containing segments. It is likely that the heating made the kinetic conditions better in the corresponding environment.

Comparing the lithium-free salt CPPC-SPE before and after heating, it is found that after heating, only a wide and weak hydroxyl absorption band appeares in the range of 3100–3700 cm−1, which indicates that the surface of the pure PPC film still forms a hydroxyl-based complex after heated, but there is no characteristic band of PC, indicating that the reaction between PPC and lithium sheet does not produce PC, and the corresponding SPE is still in a dry state. Similar to the transient complex formed by PPC and lithium ion, a complex of carbonyl and lithium ion is formed on the left side of the carbonyl group at 1800 cm−1, and this difference is likely to be caused by little dissolution of lithium hydroxide in the polymer matrixin. The reason that hydroxyl appeared is the decomposition of PPC in alkaline environment to produce hydroxyl segments.

In the comparison CPPC-SPE of 30% and lithium-free salt, it can be seen that in the high wavelength region, the band positions are almost identical, but there is a difference in intensity. Hydroxyl and hydroxy-lithium are concentrated in this region. Combined with the mechanism of PPC gelation proposed by Cui [21] as shown in Fig. 7, it can be found that the lithium hydride complex formed by the small molecular segments after the preliminary gelation of PPC is essential, and the complex is unstable, further reaction under the catalysis of metallic lithium produces monomeric PC and smaller segments. It is apparent that the addition of the electrolyte lithium salt is very advantageous for the formation of such a complex of hydroxy-lithium for accelerating the gelation of PPC. In addition to this, we have also found the O-Li+ chemical bond obtained by replacing the alcoholic hydroxyl group with lithium ions after heating the lithium cell.
Fig. 7

Gelation mechanism of PPC

[21]

5 RT conductivity of gelled film

PPC-based SPE is all solid when assembled, but in a gel state while actually operates, which is a major feature of PPC-based SPE. Therefore, it is more practical to determine the room temperature ionic conductivity after PPC gelation.

It can be seen from the Fig. 8 that the gel state electrolyte membrane of CPPC-SPE can reach the order of 10−3 S/cm at room temperature [1], which is equivalent to the liquid electrolyte. Compared to the ungelatinized PPC film, the RT conductivity increases by nearly two orders of magnitude, which is very beneficial for cell performance.
Fig. 8

Ionic conductivity of CPPC-SPE in RT after gelation

As be seen from the Fig. 8, the RT conductivity of the gel electrolyte membrane of 10% lithium salt and 30% lithium salt is only double the gap, which is almost same to show in non-power devices in performance [1]. However, for the process performance, since the organic lithium salt is highly viscous, the electrolyte membrane becomes wet and sticky, and this characteristic is remarkable at a high lithium salt concentration, which is disadvantageous for the scale production of the PPC-based SPE. Therefore, considering the comprehensive consideration, it is recommended to use a low concentration of lithium salt.

6 Cell performance

The above-prepared CPPC-SPE with a LITFSI content of 10 wt% assembled 2025 button cell matching positive electrode of NCM523 were tested for cycle performance. The charge and discharge system was: “constant current (CC) charge–constant voltage (CV) charge–constant current discharge”, the voltage interval was 2.8–4.3 V.

As can be seen from the Fig. 9a, the capacity–voltage curve of the cell is the same as that of the conventional liquid cell [26]. However, the cell’s first cycle efficiency is lower, mainly because the cell has been overcharged in the first cycle. This is because there is a electron exchange reaction, the oxidation state ions of the transition metal oxide are reduced by PPC on the cathode reported by Cui [27], thus causing a fake high charge capacity. During the entire charge and discharge process, The proportion of capacity occupied by CV charging gets higher and higher, and the amplitude of the rise is increasing, eventually exceeding the charging capacity of the CC stage. When the ratio of the CV charging capacity starts to rise, the discharge capacity does not increase significantly, obviously, which indicates that the charging capacity in the CV is not all used for the deintercalation of lithium ions from the positive material, but other side reactions have occurred.
Fig. 9

a Curve of efficiency/capacity; b curve of voltage–CV charging capacity; c charge–discharge capacity cycle curve; d curve of electrochemical window

Comparing the electrochemical window obtained by the test, it can be found that although the oxidation current of the electrolyte membrane is significantly increased at 4.6 V, However, it can be seen that after amplification, the change trend of the oxidation current has increased at 3.8 V, and further increases at 4.3 V. Therefore, we have reason to suspect that the optimum cycle voltage of the CPPC-SPE should be 3.8 V at the highest, and the higher voltage cycle will cause continuous destruction of the electrolyte membrane, which will greatly reduce the cycle performance. Obviously, it is the gelation of PPC that causes the gelled product to not withstand a high voltage of 3.8 V or more.

7 Conclusions

Metallic lithium can degrade PPC. When lithium is dissolved in the matrix, heating greatly promotes this process, producing PC and hydroxyl-containing short chains, which is the in situ gelation of PPC-based SPE in lithium metal cell. The liquid-containing product generated by this mechanism will greatly improve the wettability of SPE to the positive and negative electrodes, which is beneficial to the performance of the battery. Anyway, in situ gelation, as an important feature of PPC-based solid electrolytes, will certainly have a certain position in the development of all-solid-state cell technology.

Notes

Funding

This study was funded by National Natural Science Foundation of China (Grant No. 51474113).

Compliance with ethical standards

Conflict of interest

The authors declare that they have no conflict of interest.

References

  1. 1.
    Goodenough JB, Kim Y (2010) Challenges for rechargeable Li batteries. Chem Mater 22:587–603CrossRefGoogle Scholar
  2. 2.
    Wang Y, Richards WD, Ong SP, Miara LJ, Kim JC, Mo Y, Ceder G (2015) Design principles for solid-state lithium superionic conductors. Nat Mater 14:1026–1031CrossRefGoogle Scholar
  3. 3.
    Bachman JC, Muy S, Grimaud A, Chang HH, Pour N, Muy S, Grimaud A, Chang HH, Pour N, Lux SF, Paschos O, Maglia F, Lupart S, Lamp P, Giordano L, Horn YS (2015) Inorganic solid-state electrolytes for lithium batteries: mechanisms and properties governing ion conduction. Chem Rev 116:140–162CrossRefGoogle Scholar
  4. 4.
    Takada K (2013) Progress and prospective of solid-state lithium batteries. Acta Mater 61:759–770CrossRefGoogle Scholar
  5. 5.
    Quartarone E, Mustarelli P (2011) Electrolytes for solid-state lithium rechargeable batteries: recent advances and perspectives. Chem Soc Rev 40:2525–2540CrossRefGoogle Scholar
  6. 6.
    Zhang J, Zang X, Wen H, Dong T, Chai J, Li Y, Chen B, Zhao J, Dong S, Ma J, Yue L, Liu Z, Guo X, Cui G, Chen L (2017) High-voltage and free-standing poly (propylene carbonate)/Li6.75La3Zr1.75Ta0.25O12 composite solid electrolyte for wide temperature range and flexible solid lithium ion battery. J Mater Chem A 5:4940–4948CrossRefGoogle Scholar
  7. 7.
    Zhou D, Zhou R, Chen C, Yee WA, Kong J, Ding G, Lu X (2013) Non-volatile polymer electrolyte based on poly (propylene carbonate), ionic liquid, and lithium perchlorate for electrochromic devices. J Phys Chem B 117:7783–7789CrossRefGoogle Scholar
  8. 8.
    Bae J, Li Y, Zhang J, Zhou X, Zhao F, Shi Y, Goodenough JB, Yu G (2018) A 3D nanostructured hydrogel-framework-derived high-performance composite polymer lithium-ion electrolyte. Angew Chem Int Ed 57:2096–2100CrossRefGoogle Scholar
  9. 9.
    Zhang X, Liu T, Zhang S, Huang X, Xu B, Lin Y, Xu B, Li L, Nan CW, Shen Y (2017) Synergistic coupling between Li6.75La3Zr1.75Ta0.25O12 and poly (vinylidene fluoride) induces high ionic conductivity, mechanical strength, and thermal stability of solid composite electrolytes. J Am Chem Soc 139:13779–13785CrossRefGoogle Scholar
  10. 10.
    Shen Y, Zhang Y, Han S, Wang J, Peng Z, Chen L (2018) Unlocking the energy capabilities of lithium metal electrode with solid-state electrolytes. Joule 2:1674–1689CrossRefGoogle Scholar
  11. 11.
    Xu L, Tang S, Cheng Y, Wang K, Liang J, Liu C, Cao YC, Wei F, Mai L (2018) Interfaces in solid-state lithium batteries. Joule 2:1991–2015CrossRefGoogle Scholar
  12. 12.
    Huang X, Zeng S, Liu J, He T, Sun L, Xu D, Yu X, Luo Y, Zhou W, Wu J (2015) High-performance electrospun poly (vinylidene fluoride)/poly (propylene carbonate) gel polymer electrolyte for lithium-ion batteries. J Phys Chem C 119:27882–27891CrossRefGoogle Scholar
  13. 13.
    Zhang J, Zhao J, Yue L, Wang Q, Chai J, Liu Z, Zhou X, Li H, Guo Y, Cui G, Chen L (2015) Safety-reinforced poly (propylene carbonate)-based All-solid-state polymer electrolyte for ambient-temperature solid polymer lithium batteries. Adv Energy Mater 5:1501082CrossRefGoogle Scholar
  14. 14.
    Dukhanin GP, Gaidadin AN, Novakov IA (2014) A solid polymeric electrolyte based on the poly (propylene carbonate)-lithium perchlorate system. Russ J Appl Chem 87:1868–1871CrossRefGoogle Scholar
  15. 15.
    Dukhanin GP, Dumler SA, Sablin AN, Novakov IA (2009) Solid polymeric electrolyte based on poly (ethylene carbonate)-lithium perchlorate system. Russ J Appl Chem 82:243–246CrossRefGoogle Scholar
  16. 16.
    Li Y, Ding F, Xu Z, Sang L, Ren L, Ni W, Liu X (2018) Ambient temperature solid-state Li-cell based on high-salt-concentrated solid polymeric electrolyte. J Power Sources 397:95–101CrossRefGoogle Scholar
  17. 17.
    Zhao J, Zhang J, Hu P, Ma J, Wang X, Yue L, Xu G, Qin B, Liu Z, Zhou X, Cui G (2016) A sustainable and rigid-flexible coupling cellulose-supported poly (propylene carbonate) polymer electrolyte towards 5 V high voltage lithium batteries. Electrochim Acta 188:23–30CrossRefGoogle Scholar
  18. 18.
    Zhang J, Yang J, Dong T, Zhang M, Chai J, Dong S, Wu T, Zhou X, Cui G (2018) Aliphatic polycarbonate-based solid-state polymer electrolytes for advanced lithium batteries: advances and Perspective. Small 14:1800821CrossRefGoogle Scholar
  19. 19.
    Zhou Q, Zhang J, Cui G (2018) Rigid-flexible coupling polymer electrolytes toward high-energy lithium batteries. Macromol Mater Eng 303:1800337CrossRefGoogle Scholar
  20. 20.
    Tominaga Y (2017) Ion-conductive polymer electrolytes based on poly (ethylene carbonate) and its derivatives. Polym J 49:291–299CrossRefGoogle Scholar
  21. 21.
    Wang C, Zhang H, Li J, Chai J, Dong S, Cui G (2018) The interfacial evolution between polycarbonate-based polymer electrolyte and Li-metal anode. J Power Sources 397:157–161CrossRefGoogle Scholar
  22. 22.
    Lin Y, Li J, Liu K, Liu Y, Liu J, Wang X (2016) Unique starch polymer electrolyte for high capacity all-solid-state lithium sulfur battery. Green Chem 18:3796–3803CrossRefGoogle Scholar
  23. 23.
    Han X, Gong Y, Fu KK, He X, Hitz GT, Dai J, Pearse A, Liu B, Wang H, Rubloff G, Mo Y, Thangadurai V, Wachsman ED, Hu L (2017) Negating interfacial impedance in garnet-based solid-state Li metal batteries. Nat Mater 16:572–579CrossRefGoogle Scholar
  24. 24.
    Wang C, Xie H, Zhang L, Gong Y, Pastel G, Dai J, Liu B, Wachsman ED, Hu L (2018) Universal soldering of lithium and sodium alloys on various substrates for batteries. Adv Energy Mater 8:1701963CrossRefGoogle Scholar
  25. 25.
    Li NW, Yin YX, Yang CP, Guo YG (2016) An artificial solid electrolyte interphase layer for stable lithium metal anodes. Adv Mater 28:1853–1858CrossRefGoogle Scholar
  26. 26.
    Chen XL, Lu WZ, Chen C, Xue MZ (2018) Improved electrochemical performance of LiNi0.5Co0.2Mn0.3O2 cathode with different carbon additives for lithium-ion batteries. Int J Electrochem Sci 13:296–304CrossRefGoogle Scholar
  27. 27.
    Li J, Dong S, Wang C, Hu Z, Zhang Z, Zhang H, Cui G (2018) A study on interfacial stability of cathode/polycarbonate interface: implication of overcharge and transition metal redox. J Mater Chem A 6:11846–11852CrossRefGoogle Scholar

Copyright information

© Springer Nature Switzerland AG 2019

Authors and Affiliations

  • Te-te He
    • 2
  • Mao-xiang Jing
    • 1
    Email author
  • Hua Yang
    • 1
  • Hao Chen
    • 1
  • Song Hua
    • 1
  • Bo-wei Ju
    • 2
  • Qian Zhou
    • 2
  • Fei-yue Tu
    • 2
  • Xiang-qian Shen
    • 1
    • 2
  • Shi-biao Qin
    • 2
    Email author
  1. 1.Institute for Advanced MaterialsJiangsu UniversityZhenjiangChina
  2. 2.Changsha Research Institute of Mining and Metallurgy, Co., Ltd.ChangshaChina

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