Synthesis and electrochemical properties of
SnO2-CuO nanocomposite powders
MA Ming-you(麻明友)1, HE Ze-qiang(何则强)1, 2, XIAO Zhuo-bing(肖卓炳)1,
HUANG Ke-long(黄可龙)2, XIONG Li-zhi(熊利芝)1, WU Xian-ming(吴显明)1
1.College of Chemistry and Chemical Engineering, Jishou University, Jishou 416000, China;
2.School of Chemistry and Chemical Engineering, Central South University, Changsha 410083, China
Received 10 April 2006; accepted 25 April 2006
Abstract: SnO2-CuO nanocomposite powders were prepared by chemical coprecipitation method using SnCl4·5H2O, NH3·H2O and Cu(NO3)2·3H2O as raw materials. The powders were characterized by thermogravimertric(TG) analysis and differential thermal analysis(DTA), X-ray diffraction(XRD), and scanning electron microscope(SEM). The electrochemical properties of SnO2-CuO and undoped SnO2 powders as anode materials of lithium ion batteries were investigated comparatively by galvanostatic charge-discharge experiments and AC impedance. The results show that SnO2-CuO nanocomposite powders with the average particle size of 87 nm can be obtained by this method. The structure of SnO2 does not change with the introduction of CuO, but the average particle size of nano-SnO2 decreases. SnO2-CuO nanocomposite powders show a reversible capacity of 752 mA·h/g and better cycleability compared with nano-SnO2. The capacity retention rates after 60 cycles of nano-SnO2-CuO and SnO2 are 93.6% and 92.0% at the charge- discharge rate of 0.1 C, respectively, which suggests that the introduction of CuO into SnO2 can improve the cycleability of nano- SnO2.
Key words: SnO2; CuO; chemical coprecipitation method; lithium ion batteries; electrochemical properties
1 Introduction
Since YOSHIO et al[1] announced the commercia- lization of tin oxide as negative electrodes of 1ithium-ion batteries, the tin oxide anode has attracted much attention due to its high specific capacity, which is about twice that of graphite, and has been considered the best candidate for lithium-ion battery anode material[2-7]. When SnO2 was used as the anode material of 1ithium- ion batteries, tin works as the virtual part, and its reversible capacity is based on the formation and decomposition of 1ithium tin alloys, LiSn, Li7Sn3, Li5Sn2, Li3Sn5, Li7Sn2 or Li22Sn5[8]. The oxygen in SnO2 can combine with lithium to form Li2O in the first cycle, which acts as the buffer for tin aggregation. Lithium intercalating in tin dioxide in the first cycle can be described by the following reactions[2 ,9, 10]:
(1)
(2)
Different synthetic techniques can make SnO2 with different particle sizes and morphologies, which can further affect its electrochemical performance. In this works, SnO2-CuO was synthesized by chemical copreci- pitation method and its electrochemical properties were investigated in detail.
2 Experimental
2.1 Preparation of SnO2-CuO
A certain amount of SnCl4·5H2O and Cu(NO3)2·3H2O at a mass ratio of w(CuO):w(SnO2) =1:10 was dissolved in de-ionized water to get a mixed aqueous solution. Then NH3·H2O was added into the solution dropwise under strong stirring to keep the pH value of the solution in the range of 8-9. When the reaction completed, an azury precipitation was formed. After aged at room temperature for 2 h, the precipitation was washed with water and ethanol until no Cl- can be detected by AgNO3 in the washing liquid. After the precipitation was dried at 105 ℃ for 4 h, it was calcined at 600 ℃ for 3 h in air to obtain the product of SnO2-CuO.
2.2 Material characterization
The thermal behavior of the precursor was investigated by thermogravimetric analysis(TGA) and differential thermal analysis(DTA) on a TGA-SDTA851e thermal analysis system(Mettler Toledo Corp) from 25℃ to 800 ℃ in Ar atmosphere at a heating rate of 10 ℃/min. The phase of the samples was characterized by X-ray diffraction(XRD, Rigaku D/MAX-gA) with a mono-chromatic Cu Kα radiation (0.1540 5 nm). The surface morphology, composition of elements of the samples were analyzed by means of scanning electron microscope (SEM, JEOL JSM 5600LV). The grain size was calculated using the Scherrer formula of D=0.89λ/ βsin θ, in which D is the crystalline size, λ is the wavelength of X-ray, and θ is the diffraction peak angle.
2.3 Electrode preparation and electrochemical chara- cterization
The SnO2-CuO was made into slurry with 80% SnO2 powder, 10% acetylene black, and 10% polyvinylidene difluoride(PVDF) in N-methyl pyrolidinone(NMP). The mixture was then coated on copper foils followed by a drying in vacuum at 120 ℃ for 10 h to obtain the SnO2-CuO electrode.
The electrochemical tests were conducted using a conventional coin-type(2025) cell, employing SnO2-CuO as positive electrode, a polypropylene microporous separator, utilizing 1.0 mol/L LiPF6 in ethylene carbonate/dimethyl carbonate (EC/DMC) (with an EC to DMC volume ratio of 1:1) as the electrolyte and lithium foil as negative electrode. The assembly was carried out in an Ar-filled glove box. The discharge-charge tests were done with a PCBT-110-8D battery tester under a constant current rate of 0.1C and a constant temperature of (25±0.01) ℃ in the voltage range of 0-1.0 V. The AC impedance measurement was carried out on CHI660B electrochemical station. Here, the discharge process means the process of Li+ insertion into SnO2-CuO electrode and the charge process means the process of Li+ de-insertion out of SnO2-CuO electrode.
3 Results and discussion
Fig.1 shows the TG-DTA curves of the precursor dried at 105 ℃. From DTA curve, a large endothermic peak appears at 123 ℃. The endothermic peak corresponds to a clear mass loss on the TG curve, which is caused by the evaporation of physically absorbed water on the surface of the precursor. Due to the decomposition of little NH4Cl impurity in the precursor, an unconspicuous endothermic peak appears at 234 ℃ and a tardigrade mass loss can be found on the TG curve. A great exothermic peak near 275 ℃ on DTA curve and obvious mass loss on TG curve are found, which may correspond to the decomposition of precursor to form SnO2, CuO and CuSnO3. Because CuSnO3 is unstable and easy to decompose and form stable SnO2-CuO, a small exothermic peak at 450 ℃ is seen in the DTA curve [11]. From the analysis of TG-DTA curves, it can be concluded that the crystallization of SnO2-CuO takes place at 250-500 ℃.
Fig.1 TG-DTA curves of precursor
The XRD patterns of SnO2-CuO and undoped SnO2 calcined at 500 ℃ for 3 h are presented in Fig.2. In the scan range from 10? to 90?, both the samples show the four major peaks (100), (101) , (200) and (211), which correspond well with that of cassiterite phase (JCPDS file 41-1445). No diffraction peaks of CuO can be seen in Fig.2, which indicates that CuO has entered the crystal lattice and SnO2-CuO solid solution is formed[12]. However, the peak half width of SnO2-CuO is wider than that of SnO2. According to Scherrer formula, we can calculate the crystal grain size of SnO2-CuO to be 87 nm,
Fig.2 XRD patterns of nano SnO2(a) and nano CuO-SnO2 powders(b) calcined at 500 ℃ for 3 h
which is smaller than that of SnO2, 92 nm. This shows the grain size of SnO2 decreases with the doping of CuO, suggesting that the growth of the crystal of SnO2 is depressed by the doping of CuO[13].
Fig.3 shows the morphologies of SnO2-CuO and undoped SnO2 calcined at 500 ℃ for 3 h. From Fig.3 we can see there is no essential difference between SnO2-CuO and undoped SnO2 and the average particle size is 80-90 nm. However, the particle size of SnO2- CuO seems to be smaller than that of the undoped SnO2, which agrees with the result of XRD analyses.
Fig.3 SEM images of nano SnO2(a) and nano SnO2-CuO(b) powders calcined at 500 ℃ for 3 h
Fig.4 shows the EDS results of nano SnO2-CuO calcined at 500 ℃ for 3 h. As can be seen in the figure, except for Sn and Cu, no other metal element can be
Fig.4 EDS results of nano SnO2-CuO powders calcined at 500℃ for 1 h
detected, which indicates that the Cu element is doped into SnO2. According to the EDS results, it can be calculated that the mass ratio of CuO to SnO2 is 1:10.1, which agrees well with the mass ratio of 1:10.0, suggesting that the obtained sample is CuO-doped SnO2.
The first discharge-charge curves of nano SnO2 and nano SnO2-CuO powders calcined at 500℃ for 3 h are shown in Fig.5. The first discharge-charge curves of nano SnO2 and nano SnO2-CuO are similar to each other, indicating that nano SnO2-CuO has a similar mechanism of Li storage as nano SnO2[2, 4]. The plateau between 1.0 V and 1.5 V in the discharging curves disappears in the latter cycle, corresponding well to the irreversible formation of Li2O and solid-electrolyte interface(SEI) in the first discharging process[14]. They can give a total theoretical irreversible capacity of about 933 and 899 mA·h/g for nano SnO2 and nano SnO2-CuO, respectively. The plateau at 0.5-0.7 V in the discharge-charge curves is due to the reversible alloying process of lithium and tin, and it is the source of reversible capacity, which is about 760 and 752 mA·h/g for nano SnO2 and nano SnO2-CuO respectively.
Fig.5 First discharge-charge curves of nano SnO2(a) and SnO2- CuO(b) (0.1C)
Fig.6 shows the variation of reversible capacity as a function of cycle number. For nano SnO2, after 60 cycles the reversible capacity remains 92.0% that of the first cycle, the average capacity fade rate is 0.13% per cycle; while for nano SnO2-CuO, the values are 93.6% and 0.11%, respectively. Compared with nano SnO2, nano SnO2-CuO anode has a smaller reversible capacity and better cycleability, which may result from the decreased mass of active material and particle size due to the doping of CuO.
Fig.7 shows the AC impedance diagram of nano SnO2-CuO anode. Two semicircles and an inclined line can be seen in the figure. The high frequency arc is attributed to the charge-transfer reaction at the interface of electrolyte and electrode. The medium frequency arc implies the formation of a new phase during the discharge and charge process, which may be caused by the formation of solid electrolyte interface(SEI) film on the surface of nano SnO2-CuO[15]. The inclined line corresponds to Warburg impedance related to the diffusion of lithium ion in nano SnO2-CuO anode [16].
Fig.6 Cycleability of nano SnO2-CuO and nano SnO2 calcined at 500 ℃ for 3 h (0.1C)
Fig.7 AC impedance diagram of nano SnO2-CuO calcined at 600 ℃ for 3 h
4 Conclusions
Nano SnO2-CuO were prepared by chemical co- precipitation method using SnCl4·5H2O, NH3·H2O and Cu(NO3)2·3H2O as raw materials. The average particle size of synthesized SnO2-CuO is 87 nm. The structure of SnO2 does not change with the introduction of CuO, but the average particle size of nano-SnO2 decreases. The nano SnO2-CuO shows a reversible capacity of 752 mA·h/g and better cycleability compared with the undoped nano-SnO2. The capacity retention rate after 60 cycles of nano SnO2-CuO and SnO2 is 93.6% and 92.0% at the charge-discharge rate of 0.1 C, respectively, which suggests that the introduction of CuO in SnO2 can improve the cycleability of nano-SnO2.
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(Edited by YUAN Sai-qian)
Foundation item: Project(05C140) supported by the Scientific Research Fund of Hunan Provincial Education Department
Corresponding author: MA Ming-you; Tel: +86-743-8564088; E-mail: mamy_9589@163.com