Trans. Nonferrous Met. Soc. China 28(2018) 1397-1403

Enhanced cycling stability of Mg-F co-modified LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z for lithium-ion batteries

Qi-chao CHEN, Guan-jie YAN, Li-ming LUO, Fei CHEN, Tang-feng XIE, Shi-can DAI, Ming-liang YUAN

School of Minerals Processing and Bioengineering, Central South University, Changsha 410083, China

Received 13 March 2017; accepted 18 September 2017

Abstract: The layered LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z (0≤y≤0.12, 0≤z≤0.08) cathode materials were synthesized by combining co-precipitation method and high temperature solid-state reaction, with the help of the ball milling, to investigate the effects of F-Mg doping on LiNi_0.6Co_0.2Mn_0.2O₂. Compared with previous studies, this doping treatment provides substantially improved electrochemical performance in terms of initial coulombic efficiency and cycle performance. The LiNi_0.6Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 electrode delivers an high capacity retention of 98.6% during the first cycle and a discharge capacity of 189.7 mA·h/g (2.8-4.4 V at 0.2C), with the capacity retention of 96.3% after 100 cycles. And electrochemical impedance spectroscopy(EIS) results show that Mg-F co-doping decreases the charge-transfer resistance and enhances the reaction kinetics, which is considered to be the major factor for higher rate performance. It is demonstrated that LiNi_0.6Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 is a promising cathode material for lithium-ion batteries for excellent electrochemical properties.

Key words: nickel-rich cathode material; F-Mg doping; high columbic efficiency; cycling stability

1 Introduction

With the continuous development of society, energy consumption has become a global problem, so there is drastically increased demand for new green energy [1]. As an energy storage and conversion device, the lithium-ion battery (LIB) shows many advantages, such as large energy density, high transform efficiency, little pollution and portability [2]. LIBs have been used in a broad range of applications, like cell phone, notebook, electric car and medical equipment [3]. Cathode material plays an important role in LIB, and the cathode material directly determines its performance.

Traditional research on cathode materials of LIB mainly concentrated on the transition metal oxides with layered structure such as LiNiO₂, LiCoO₂, LiMnO₂ and their derivatives. LiCoO₂ is one of the first commercial LIB cathode material, but its application is limited because of the scarce cobalt resources, high price and toxicity [4-6]. The difficult preparation and over  charge security of LiNiO₂ seriously restrict its commercialization [7-9]. The layered LiMnO₂ has a high theoretical specific capacity (C_m) of 285 mA·h/g. However, its structure easily changes to the spinel structure during the charging and discharging process, resulting in the rapid decay of specific capacity [10-12]. Recently, intensive efforts have been directed towards the layered Li-Ni-Co-Mn-O (e.g. LiNi_0.5Mn_0.3Co_0.2O₂) composites for their high capacity, good cycling stability and security [13-18]. Among them, LiNi_0.6Co_0.2Mn_0.2O₂ [19,20] has been investigated as a promising cathode material. In order to increase the availability of cathode material in electric vehicles and other high-power devices, it is necessary to improve its electrochemical performance.

At present, researchers at home and abroad have improved the performance of materials by doping and coating [21-24]. So far, Mg has been used successfully to improve the cycling stability of cathode materials such as LiNi_1-xCo_xO₂ [25] and LiLi_0.2Ni_0.2Mn_0.6O₂ [26]. The improved performance is attributed to the enhanced conductivity and structural stability [25]. Fluorine substitution at the oxygen site has been reported to be effective for improving cycle life and rate performance of the cathode active materials for lithium-ion batteries [27,28]. By understanding the effect of F-Mg doping on the electrochemical performance of electrode materials, the rate and cycling properties of electrode materials can be improved effectively. Thus, F-doping can be widely applied in the cathode materials. In this work, LiNi_0.6Co_0.2Mn_0.2O₂ was prepared by a co-precipitation method, and material was doped with Mg and F elements. The effects of doping elements and doping ratio on electrochemical were investigated.

2 Experimental

2.1 Preparation of cathode materials

The precursor Ni_0.6Co_0.2Mn_0.2-yMgy(OH)₂ was prepared by the co-precipitation. Nickel sulfate (NiSO₄·6H₂O), cobalt sulfate (CoSO₄·7H₂O), manganese sulfate (MnSO₄·H₂O) and magnesium sulfate (MgSO₄) were dissolved in deionized water in a certain molar ratio of Co:Ni:(Mn+Mg)=2:6:2 with different doping amounts of Mg (0, 3%, 6%, 9% and 12%). Then, sodium hydroxide (NaOH) solution was added into the mixture with 1:1.2 (V/V) of NH₃/H₂O to obtain a solution with the pH value of about 11. It was subsequently stirred under 1000 r/min at 50 °C for 12 h to react, then rested for 10 h. After washing, it was dried at 120 °C for 8 h to obtain precursor Ni_0.6Co_0.2Mn_0.2-yMgy(OH)₂. Then, the dried precursor was ground with Li₂CO₃ and LiF with a certain molar ratio of (OH^-+F^-):Li⁺=1:1, when the doping amounts of F^- were 0, 2%, 4%, 6% and 8%, respectively, to obtain different mixtures. The powders were subsequently annealed at 900 °C in air for 20 h followed by a natural cooling step to obtain LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z powders.

2.2 Physical characterization

The powder X-ray diffraction (XRD, DX-2700) measurement, using Cu K_α radiation (λ=0.154 nm) in the range of 10°-80° (2θ) with a step width of 0.02°, was used to identify the crystalline phase. The particle size and morphology of the LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z powders were observed by a scanning electron microscope (JSM-6360LV) with an accelerating voltage of 20 kV.

2.3 Electrochemical properties evaluation

The electrochemical characterization was performed using CR2025 coin-type cell by GAMRY Reference 600 electrochemical workstation. For positive electrode fabrication, the prepared powders were mixed with 10% (mass fraction) of carbon black and 10% (mass fraction) of polyvi-nylidene fluoride (PVDF) in N-methyl pyrrolidinone (NMP) until slurry was obtained. And then, the blended slurries were pasted onto an aluminum current collector, and the electrode was dried at 120 °C for 10 h in vacuum. The test cell consisted of the positive electrode and lithium foil (negative  electrode) separated by a porous polypropylene (PP) film, with    1 mol/L LiPF₆ in EC:EMC:DMC (1:1:1 in volume) as the electrolyte. The assembly of the cells was carried out in a dry Ar-filled glove box. The cells were charged and discharged over a voltage range of 2.8 to 4.4 V versus Li/Li⁺ electrode at room temperature. Cyclic voltammograms were tested in the three-electrode system using metallic foils as both counter and reference electrodes at a scanning rate of 0.1 mV/s in the voltage range of 3.0-4.8 V. EIS experiments were performed with a 10 mV voltage magnitude in the range of 0.01 Hz-100 kHz.

3 Results and discussion

3.1 XRD and chemical components analysis

Figure 1 shows the XRD patterns of prepared LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z (y=0.09, z=0.04). As shown in Fig. 1, all the reflection peaks indicate that the samples have standard α-NaFeO₂-type layered structure with the space group R3(_)m [29], expect for the super lattice ordering between 20° and 25°. Many researches point out that these super lattice peaks are caused by the LiMn₆ cation ordering which exists in the transition metal layers of Li₂MnO₃ [30]. Another observation in the XRD patterns is the clear splitting of the (006)/(102) and (108)/(110) peaks, indicating that the materials have a well-organized layered structure [31]. No peak of any impurity phase is detected in the XRD patterns of Mg-F co-doped samples, indicating that the small amount of Mg-F co-doping has no impact on the significant structure of the cathode material.

Fig. 1 XRD patterns of pristine and Mg-, F-doped cathode materials

The lattice parameters of all samples are calculated and summarized in Table 1. The c/a ratios of all samples are greater than 4.9, which is well known for a material with layered characteristic [32,33]. As the ionic radius of Mg²⁺ (0.72 ) is larger than that of Ni²⁺ (0.69 ), Mn⁴⁺ (0.53 ) and Co³⁺ (0.54 ), the lattice parameter c indicates that interlayer spacing increases after doping. The process of Li⁺ intercalation/deintercalation will be facilitated by the enlargement of c value.

The intensity ratio (R) of I(003)/I(104) is sensitive to the cation distribution in the lattice and the degree of cation mixing of materials [34]. When the R value is higher, the degree of cation mixing is lower. It is  reported that the undesirable cation mixing would appear when R is smaller than 1.2 [32,33]. The R value of all samples is larger than 1.2, which implies that the cation mixing is very weak for all samples. The value of R increases after doping. It can be expected that the undoped samples are more prone to cation mixing than the Mg-F co-doped ones. This is because the Mg element is more likely to occupy the Li site because of a small difference in size between Mg²⁺ (0.72 ) and Li⁺ (0.76 ), in contrast with other cations: Mn⁴⁺ (0.53 ), Co³⁺ (0.54 ) and Ni²⁺ (0.69 ). The cation mixing of Li/Mg exchange will restrain that of Li/Ni exchange, the latter might induce structural collapse by the radius changes of nickel ions (Ni²⁺/Ni³⁺/Ni⁴⁺) during charge and  discharge process [35]. In addition, the F^- doping can also improve the crystallinity of materials. Because the electronegativity of F^- is stronger than that of O^2-, the doping of F can hinder the transformation of Ni⁴⁺ to Ni²⁺, which can also restrain the cation mixing (Li/Ni exchange).

Table 2 lists the chemical composition of prepared LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z (y=0.09, z=0.04). As we known, Li will loss at the temperature of 900 °C. It can be seen that, by increasing the content of lithium source, the lithium content of positive electrode material in a reasonable range, and theoretical molar ratio of positive electrode material are obtained.

3.2 SEM of synthesized LiNi_0.6Co_0.2Mn_0.2-yMg_yO_1.96- F_0.04 samples

The microstructures of LiNi_0.6Co_0.2Mn_0.2-yMg_y- O_1.96F_0.04 (y=0, 0.06, 0.09, 0.12) powders are illustrated in Fig. 2, where a small change in the morphology of particles by Mg doping can be identified. For the samples with y=0, the particle size is about 0.5 μm. With increasing amount of Mg²⁺ doped, the particle size of the prepared powders slightly decreases. It could be noticed that y=0.09 exhibits the relative uniform particle size, there are some primary particles and larger secondary ones while y=0, 0.06, 0.12.

3.3 Electrochemical performance

To investigate the effect of F-Mg doping on the electrochemical properties of cathode materials, the charge-discharge tests were carried out at the rate of 0.2C in the voltage range of 2.8-4.4 V at room temperature. As seen in Fig. 3, the specific capacities of the first charging and discharging test of three doped materials were compared. The initial charge capacities  of LiNi_0.6Co_0.2Mn_0.2O₂, LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04, and LiNi_0.6Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 are 201.5, 188.9 and 192.4 mA·h/g, and the discharge capacities are 180.3, 181.6 and 189.7 mA·h/g, respectively. The correspon-ding coulombic efficiencies are 89.5%, 96.1% and 98.6%, respectively. It is clearly seen that the electrode reaction reversibility is enhanced considerably when the pristine cathode powder is doped by F-Mg. The F doping leads to deceasing the expansion rate of the crystal lattice c, which improves the stability of the layered structure, so that a small amount of F-doped samples present excellent cycle properties. Although Mg²⁺ has no electrochemical activity, it plays a role in supporting inter-layers when the crystal lattice distortion is caused by the change of valence state of nickel during the charging-discharging process. Accordingly, the F-Mg doping is beneficial to the improvement of coulombic efficiency.

Table 1 Lattice parameters of pristine and F-, Mg-doped cathode materials

Table 2 Chemical composition of positive electrode materials

Fig. 2 SEM images of LiNi_0.6Co_0.2Mn_0.2-yMg_yO_1.96F_0.04 samples calcined at 900 °C for 20 h

Fig. 3 Initial charge-discharge curves of LiNi_0.6Co_0.2Mn_0.2-y- Mg_yO_2-zFz samples

Figure 4 compares the cycling performance of LiNi_0.6Co_0.2Mn_0.2O₂, LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04, LiNi_0.6- Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 samples. The electrochemical cycling performance was evaluated in the Li/LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z cell configuration at room temperature in the voltage range of 2.8-4.4 V at 0.2C charge rate. As seen in Fig. 4, the specific capacities for LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z (y=0.09, z=0.04) samples at 0.2C discharge rates are higher than that for pristine LiNi_0.6Co_0.2Mn_0.2O₂. LiNi_0.6Co_0.2Mn_0.11Mg_0.09-O_1.96F_0.04 demonstrates remarkably improving the specific capacity and cycling performance. From Fig. 4(a), at 0.2C discharge rate, the specific capacity of un-doped LiNi_0.6Co_0.2Mn_0.2O₂ is only 155.4 mA·h/g after 100 cycles, with capacity retention of 86.2%. Whereas, these values of LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04, LiNi_0.6Co_0.2- Mn_0.11Mg_0.09O_1.96F_0.04 are 171.9 and 182.6 mA·h/g, with capacity retentions of 94.7% and 96.3%, respectively. This result is expected because of the higher electronic conductivity of Mg-F-substituted LiNi_0.6Co_0.2Mn_0.2O₂ compared with the pristine samples. These results indicate that Mg-F substitution can improve the electronic conductivity, diffusion of Li⁺ and cycling stability. Indeed, the sample of LiNi_0.6Co_0.2Mn_0.11- Mg_0.09O_1.96F_0.04 shows the best electrochemical performance.

Fig. 4 Cycling performance of LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zFz samples at 0.2C discharge rate

Figure 5 shows the alternating current (AC) impedance plots of LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 and LiNi_0.6Co_0.2Mn_0.2O₂ electrodes at about 3 V. A semicircle was observed to center on the real axis in the high frequency range. In the low frequency range, a straight line with an angle of 45° to the real axis corresponds to the Warburg impedance. The high frequency semicircle is related to the charge-transfer resistance (R_ct) and the double-layer capacitance. The low frequency tails resulted from the diffusion of Li⁺ in the bulk active mass. In the case of LiNi_0.6Co_0.2Mn_0.2O₂, the diameter of the semicircle significantly depends on the potential during charging, indicating that the film formation process is dependent on the Li⁺ content. On the other hand, the charge-transfer resistance, shows a greater dependence on the lithium insertion and extraction levels. In the highly charged states, the sample was found to give low R_ct values. Comparing the diameters of the semicircle of the above two systems, it can be found that LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 showed lower R_ct value than LiNi_0.6Co_0.2Mn_0.2O₂, indicating that the F-doping may cause some defects in the LiNi_0.6Co_0.2Mn_0.2O₂ system, which increases the electronic conductivity and improves the Li⁺ kinetic behavior.

Fig. 5 Nyquist plots of LiNi_0.6Co_0.2Mn_0.2O₂ (a) and LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 (b)

Figure 6 shows the AC impedance plots of LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 and LiNi_0.6Co_0.2Mn_0.11Mg_0.09- O_1.96F_0.04. This result is well in accordance with the rate capability. The decreased resistance can be attributed to the enhanced conductivity by Mg-F doping. All in all, the doped samples reveal much lower values compared with the ones for pristine sample, which can be ascribed to three reasons: 1) the doping particles possess more 3D channels for Li diffusion; 2) the doping treatment also leads to a collapse of Ni segregation which could suppress negative effects on fast transportation of Li between terminated surfaces and the bulk; 3) the doping particle may provide better surface conductivity leading to significantly reduced R_ct. In fact, such observations on EIS are consistent with the results obtained from electrochemical testing.

Fig. 6 Nyquist plots of LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 (a) and LiNi_0.6Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 (b)

Cyclic voltammetry (CV) measurements were carried out to compare electrochemical behaviors of the electrodes at a sweep rate of 0.1 mV/s. The peak potentials and peak current in the CV curve represent the electrochemical characteristics of the materials and reveal the phase transitions that occur during detercalation/intercalation of Li ions. As shown in Fig. 7, all curves of the electrodes showed a similar profile. The appearance of only one couple of peaks in the LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z/Li cell between 3.2 and  4.6 V means that no structural transitions exist from hexagonal to monoclinic, which is believed to limit the reversible charge/discharge capacity in LiCoO₂. The oxidation peak of LiNi_0.6Co_0.2Mn_0.2O₂ was observed at around 4.05 V, coupled with the reduction peak at   3.67 V; the oxidation peak of LiNi_0.6Co_0.2Mn_0.2O_1.96F_0.04 was observed at around 4.03 V, coupled with the reduction peak at 3.79 V. In the case of LiNi_0.6- Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 electrode, the oxidation peaks shifted down to 3.98 V, while the reduced peaks shifted up to 3.81 V. Namely, the potential difference for the redox couples of LiNi_0.6Co_0.2Mn_0.11Mg_0.09O_1.96F_0.04 was reduced, which indicates that the reversibility of the electrode reaction could be enhanced by Mg-F co-doping.

Fig. 7 CV curves of LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zFz samples

4 Conclusions

1) XRD results of Mg-F-co-doped LiNi_0.6Co_0.2- Mn_0.2-yMg_yO_2-zF_z powders show that they exhibit similar XRD patterns as those of pristine cathode materials.

2) Electrochemical charge/discharge measurements in lithium-ion cells indicate that the Mg-F-co-doped samples exhibit high discharge capacity and superior rate capability. The F-Mg-doped LiNi_0.6Co_0.2Mn_0.2O₂ has better electrochemical performance than the bare LiNi_0.6Co_0.2Mn_0.2O₂. At 0.2C rate, the initial coulombic efficiency of the LiNi_0.6Co_0.2Mn_0.2O₂ is improved from 89.5 % to 98.6 % by F-Mg co-doping. And the capacity retention is improved from 86.2% to 96.3 % after 100 cycles at 0.2C rate.

3) EIS results show that Mg-F doping decreases the charge-transfer resistance and enhances the reaction kinetics, which is considered to be the major factor for high rate performance. In brief, LiNi_0.6Co_0.2Mn_0.11- Mg_0.09O_1.96F_0.04 is characterized to be a promising cathode material for lithium ion batteries.

References

[1] DUNN B, KAMATH H, TARASCON J M. Electrical energy storage for the grid: A battery of choices [J]. Science, 2011, 334(6058): 928-935.

[2] WU H B, CHEN J S, HNG H H, LOU X W. Nanostructured metal oxide-based materials as advanced anodes for lithium-ion batteries [J]. Nanoscale, 2012, 4(8): 2526-2542.

[3] ZUBI G, DUFO L R, PARDO N, PASAOGLU G. Concept development and techno-economic assessment for a solar home system using lithium-ion battery for developing regions to provide electricity for lighting and electronic devices [J]. Energy Conversion & Management, 2016, 122: 439-448.

[4] SCHIPPER F, AURBACH D. A brief review: Past, present and future of lithium ion batteries [J]. Russian Journal of Electrochemistry, 2016, 52(12): 1095-1121.

[5] YUAN Qing-feng, ZHAO Feng-gang, WANG Wei-dong, ZHAO Yan-ming, LIANG Zhi-yong, YAN Dan-lin. Overcharge failure investigation of lithium-ion batteries [J]. Electrochimica Acta, 2015, 178: 682-688.

[6] SHIM J H, LEE S, PARK S S. Effects of MgO coating on the structural and electrochemical characteristics of LiCoO₂ as cathode materials for lithium ion battery [J]. Chemistry of Materials, 2014, 26(8): 2537-2543.

[7] MUKAI K, SUGIYAMA J, IKEDO Y, AOKI Y, ANDREICA D, AMATO A. Structural and magnetic nature for fully delithiated Li_xNiO₂: Comparative study between chemically and electrochemically prepared samples [J]. Journal of Physical Chemistry C, 2010, 114(18): 8626-8632.

[8] LI Yan, LIU Kai-yu, Lü Mei-yu, WEI Lai, ZHONG Jian-jian. Synthesis, characterization and electrochemical performance of AlF₃-coated Li_1.2(Mn_0.54Ni_0.16Co_0.08)O₂ as cathode for Li-ion battery [J]. Transactions of Nonferrous Metals Society of China, 2014, 24(11): 3534-3540.

[9] RIM H, PARK H R, SONG M Y. Electrochemical performance of cobalt-substituted lithium nickel oxides synthesized from lithium and nickel carbonates and cobalt oxide [J]. Ceramics International, 2013, 39(2): 917-923.

[10] SEYMOUR I D, WALES D J, GREY C P. Preventing structural rearrangements on battery cycling: A first principles investigation of the effect of dopants on the migration barriers in layered Li_0.5MnO₂ [J]. Journal of Physical Chemistry C, 2016, 120(35): 19521-19530.

[11] PANG W K, LEE J Y, WEI Y S, WU S H. Preparation and characterization of Cr-doped LiMnO₂ cathode materials by Pechini's method for lithium ion batteries [J]. Materials Chemistry & Physics, 2013, 139(1): 241-246.

[12] JI Hong-mei, MIAO Xiao-wei, WANG Lu, QIAN Bing, YANG Gang. Effects of microwave-hydrothermal conditions on the purity and electrochemical performance of orthorhombic LiMnO₂ [J]. Acs Sustainable Chemistry & Engineering, 2013, 2(2): 359-366.

[13] DONG Tao, YU Xian-jin, ZHANG Li-peng, YANG Ping. Synthesis and properties of cathode materials xLi₂MnO₃·(1-x)LiMn_1/3Ni_1/3- Co_1/3O₂ for Li-ion batteries [J]. Journal of Nanoscience & Nanotechnology, 2014, 14(4): 3041-3045.

[14] NOH H J, YOUN S, CHONG S Y, SUN Y K. Comparison of the structural and electrochemical properties of layered Li[Ni_xCo_yMn_z]O₂ (x=1/3, 0.5, 0.6, 0.7, 0.8 and 0.85) cathode material for lithium-ion batteries [J]. Journal of Power Sources, 2013, 233: 121-130.

[15] PAN Cheng-chi, Zhu Yi-rong, YANG Ying-chang. HOU Hong-shuai, JING Ming-jun, SONG Wei-xin, YANG Xu-ming, JI Xiao-bo. Influences of transition metal on structural and electrochemical properties of Li[Ni_xCo_yMn_z]O₂ (0.6≤x≤0.8) cathode materials for lithium-ion batteries [J]. Transactions of Nonferrous Metals Society of China, 2016, 26(5): 1396-1402.

[16] MARTHA S K, SCLAR H, FRAMOWITZ Z S, KOVACHEVA D, SALIYSKI N, GOFER Y, SHARON P, GOLIK E, MARKOVSKY B, AURBACH D. A comparative study of electrodes comprising nanometric and submicron particles of LiNi_0.50Mn_0.50O₂, LiNi_0.33Mn_0.33Co_0.33O₂, and LiNi_0.40Mn_0.40Co_0.20O₂ layered compounds [J]. Journal of Power Sources, 2009, 189(1): 248-255.

[17] HWANG S, KIM S M, BAK S M, KIM S Y, CHO B W, CHUNG K Y, LEE J Y, STACH E A, CHANG W. Using real-time electron microscopy to explore the effects of transition-metal composition on the local thermal stability in charged Li_xNi_yMn_zCo_1–y–zO₂ cathode materials [J]. Chemistry of Materials, 2015, 27(11): 3927-3935.

[18] DENG Long-zheng, WU Feng, GAO Xu-guang, LIU Zhen-tian, XIE Hai-ming. Synthesis and electrochemical properties of LiNi_0.87Co_0.10Mg_0.03O₂ cathode materials [J]. Transactions of Nonferrous Metals Society of China, 2015, 25(2): 527-532.

[19] CAO Hui, ZANG Yao, ZANG Jian, XIA Bao-jia. Synthesis and electrochemical characteristics of layered LiNi_0.6Co_0.2Mn_0.2O₂ cathode material for lithium ion batteries [J]. Solid State Ionics, 2005, 176(13-14): 1207-1211.

[20] Na Y K, YIM T, SONG J H, YU J S, LEE Z. Microstructural study on degradation mechanism of layered LiNi_0.6Co_0.2Mn_0.2O₂ cathode materials by analytical transmission electron microscopy [J]. Journal of Power Sources, 2016, 307: 641-648.

[21] XIANG Yan-hong, LI Jian, WU Xian-wen, LIU Zhi-xiong, XIONG Li-zhi, HE Ze-qiang, YIN Zhou-lan. Synthesis and electrochemical characterization of Mg-doped Li-rich Mn-based cathode material [J]. Ceramics International, 2016, 42(7): 8833-8838.

[22] WANG Ding, LI Xin-hai, WANG Zhi-xing, GUO Hua-jun, XU Yan, FAN Yu-lei, RU Juan-jian. Role of zirconium dopant on the structure and high voltage electrochemical performances of LiNi_0.5Co_0.2Mn_0.3O₂ cathode materials for lithium ion batteries [J]. Electrochimica Acta, 2015, 188: 48-56.

[23] SHI Yang, ZHANG Ming-hao, QIAN Dan-na, MENG Y S. Ultrathin Al₂O₃ coatings for improved cycling performance and thermal stability of LiNi_0.5Co_0.2Mn_0.3O₂ cathode material [J]. Electrochimica Acta, 2016, 203: 154-161.

[24] LIU Si-yang, ZHANG Cong-cong, SU Qi-li, LI Liang-yu, SU Jun-ming, HUANG Tao, CHEN Yan-bin, YU Ai-shui. Enhancing electrochemical performance of LiNi_0.6Co_0.2Mn_0.2O₂ by lithium-ion conductor surface modification [J]. Electrochimica Acta, 2016, 224: 171-177.

[25] NITHYA C, DEVI S B, GOPUKUMAR S. Role of Mg dopant on the electrochemical performance of LiNi_0.5Co_0.5O₂, cathode materials for lithium rechargeable batteries [J]. Journal of Materials Science, 2012, 47(19): 6784-6791.

[26] WANG Dan, HUANG Yan, HUO Zhen-qing, CHEN Li. Synthesize and electrochemical characterization of Mg-doped Li-rich layered Li[Li_0.2Ni_0.2Mn_0.6]O₂ cathode material [J]. Electrochimica Acta, 2013, 107(3): 461-466.

[27] ZHONG Sheng-kui, LIU Le-tong, LIU Jie-qun, WANG Jian, YANG Jian-wen. High-rate characteristic of F-substitution Li₃V₂(PO₄)₃ cathode materials for Li-ion-batteries [J]. Solid State Communications, 2009, 149(39-40): 1679-1683.

[28] LIAO Xiao-zhen, HE Yu-shi, MA Zi-feng, ZHANG Xiao-ming, WANG Liang. Effects of fluorine-substitution on the electrochemical behavior of LiFePO₄/C cathode materials [J]. Journal of Power Sources, 2007, 174(2): 720-725.

[29] YI Ting-feng, HAN Xiao, YANG Shuang-yuan, ZHU Yan-rong. Enhanced electrochemical performance of Li-rich low-Co Li_1.2Mn_0.56Ni_0.16Co_0.08-xAl_xO₂ (0≤x≤0.08) as cathode materials [J]. Science China Materials, 2016, 59(8): 618-628.

[30] YU Hai-jun, ZHOU Hao-shen. High-energy cathode materials (Li₂MnO₃-LiMO₂) for lithium-ion batteries [J]. Journal of Physical Chemistry Letters, 2013, 4(8): 1268-1280.

[31] ZHANG Xi-hui, YU Chuang, HUANG Xiang-dong, ZHENG Jiang, GUAN Xiang-feng, LUO Dong, LI Li-ping. Novel composites Li[Li_xNi_0.34-xMn_0.47Co_0.19]O₂ (0.18≤x≤0.21): Synthesis and application as high-voltage cathode with improved electrochemical performance for lithium ion batteries [J]. Electrochimica Acta, 2012, 81: 233-238.

[32] WANG Jun, ZHANG Ming-hao, TANG Chang-lin, XIA Yong-gao, LIU Zhao-ping. Microwave-irradiation synthesis of Li_1.3Ni_xCo_yMn_1-x-yO₂ cathode materials for lithium ion batteries [J]. Electrochimica Acta, 2012, 80(1): 15-21.

[33] YU Chuang, LI Guang-she, GUAN Xiang-feng, ZHENG Jing, LI Li-ping. Composites Li_1+xMn_0.5+0.5xNi_0.5-0.5xO₂ (0.1≤x≤0.4): Optimized preparation to yield an excellent cycling performance as cathode for lithium-ion batteries [J]. Electrochimica Acta, 2012, 61: 216-224.

[34] LIANG Long-wei, DU Ke, PENG Zhong-dong, CAO Yan-bing, DUAN Jian-guo, JIANG Jian-bing, HU Guo-rong. Co–precipitation synthesis of Ni_0.6Co_0.2Mn_0.2(OH)₂ precursor and characterization of LiNi_0.6Co_0.2Mn_0.2O₂ cathode material for secondary lithium batteries [J]. Electrochimica Acta, 2014, 130: 82-89.

[35] HUANG Zhen-jun, WANG Zhi-xing, ZHENG Xiao-bo, GUO Hua-jun, LI Xin-hai, JING Qun, YANG Zhi-hua. Structural and electrochemical properties of Mg-doped nickel based cathode materials LiNi_0.6Co_0.2Mn_0.2-xMg_xO₂ for lithium ion batteries [J]. RSC Advances, 2015, 5(108): 88773-88779.

循环性能改善的F-Mg共改性LiNi_0.6Co_0.2Mn_0.2-yMg_yO_2-zF_z锂离子电池材料

陈启超，闫冠杰，罗利明，陈 飞，谢堂锋，戴世灿，袁明亮

中南大学 资源加工与生物工程学院，长沙 410083

摘  要：结合共沉淀法和球磨辅助下的高温固相法，合成层状氧化物正极材料Li[Ni_0.6Co_0.2Mn_0.2-yMg_y]O_2-zF_z (0≤y≤0.12, 0≤z≤0.08)，探究F-Mg掺杂对LiNi_0.6Co_0.2Mn_0.2O₂材料的影响。与以往的研究相比，这种掺杂处理在首次库仑效率和循环性能方面的电化学性能得到实质改善。在充放电倍率为0.2C和电压范围为2.8~4.4 V的条件 下，Li[Ni_0.6Co_0.2Mn_0.11Mg_0.09]O_1.96F_0.04的首次放电比容量和库伦效率分别为189.7 mA·h/g和98.6%，100次循环后容量保持率为96.3%。电化学阻抗谱(EIS)结果表明，Mg-F掺杂降低了电荷转移电阻，从而提高了反应动力学，这是材料具有更高倍率性能的主要原因。由于Li[Ni_0.6Co_0.2Mn_0.11Mg_0.09]O_1.96F_0.04具有优异的电化学性能，被看作是很有前景的新型锂离子电池正极材料。

关键词：高镍正极材料；F-Mg掺杂；高库伦效率；循环稳定性

 (Edited by Xiang-qun LI)

Foundation item: Project (1114022-15) supported by the Major Science and Technology Research Projects of Guangxi Province, China

Corresponding author: Ming-liang YUAN; Tel/Fax: +86-731-88877209; E-mail: mlydoc@126.com

DOI: 10.1016/S1003-6326(18)64778-8