In situ polymerization preparation and characterization of Li4Ti5O12-polyaniline anode material
HE Ze-qiang(何则强)1, 2, XIONG Li-zhi(熊利芝)1, 2, CHEN Shang(陈 上)1,
WU Xian-ming(吴显明)1, LIU Wen-ping(刘文萍)1, HUANG Ke-long(黄可龙)2
1. College of Biology and Environmental Sciences, Jishou University, Jishou 416000, China;
2. School of Chemistry and Chemical Engineering, Central South University, Changsha 410083, China
Received 6 July 2009; accepted 30 December 2009
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Abstract:
Li4Ti5O12 powders were prepared by so-gel method using tetrabutyl titanate, lithium acetate and absolute alcohol as starting materials. Li4Ti5O12-polyaniline (Li4Ti5O12-PAn) composite was prepared by in situ polymerization method using aniline, ammonium persulfate and hydrochloricarried as starting materials. Li4Ti5O12-PAn composite was characterized by X-ray diffractometry (XRD), infrared spectrum (IR) combined with electrochemical tests. The results show that the electrical conductivity is enhanced obviously due to the introduction of PAn to Li4Ti5O12. Li4Ti5O12-PAn composite exhibits better high-rate capability and cyclability than Li4Ti5O12. The composite can deliver a specific capacity of 191.3 and 148.9 mA?h/g, only 0.13% and 0.61% of the capacity is lose after being discharged 80 times at 0.1C and 2.0C, respectively.
Key words:
Li4Ti5O12; polyaniline; in situ polymerization method; lithium ion batteries;
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1 Introduction
Due to its good structural stability (zero-strain insertion material)[1-2] and satisfactory safety in the charge–discharge process, Li4Ti5O12 is thought as a good anode material for asymmetrical mixed battery and lithium ion batteries with high power. However, lower lithium-ion conductivity and low electronic conductivity of Li4Ti5O12 lead to poor rate capability[3-6]. To overcome this shortcoming, many methods have been developed, such as sol-gel, doping and nanotechnologies [1-2, 7]. The results showed that an electronically conductive agent such as Ag was very useful to improve the high-rate performance of Li4Ti5O12[8]. However, the high cost of Ag urges us to develop new conducting additive. To find a cheaper conducting additive is one of the keys for the practical application of Li4Ti5O12. Carbon is a good conducting material and used widely in lithium ion batteries. If Li4Ti5O12 is coated with carbon on its surface, the good conductivity of carbon can make up for the poor conductivity of Li4Ti5O12 and improve its electrochemical properties. GUERFI et al[9-10] investigated the effects of carbon black, high-surface- area carbon, graphite and carbonized polymer on the structure, morphology and electrochemical properties. According to their results, the carbon has three roles as follows: 1) As reducing agent, the carbon improves the reaction in the bulk powders and increases lithium diffusion in the particles to enhance complete transformation; 2) The carbon additive helps to reduce the particle size and produce an agglomerate of small particles in a chain-like structure; 3) The carbon increases the inter-particle contact and disturbs the undesirable particle growth. Hence, it is possible to obtain Li4Ti5O12 material with good performance by using different types of carbons. HE et al[11] have reported Li4Ti5O12-C composite synthesized by sol-gel method to improve the electrochemical properties, especially the high rate cycling performance of Li4Ti5O12.
Recently, the conducting polymer has been studied as an additive to improve the performances of cathode and anode materials in lithium ion batteries[12-14]. The conducting polymer composites exhibit good charge-discharge properties, indicating clearly that the conducting polymer can work as a conducting matrix for the particles of electrode. HE et al[15] have reported the SnO2-polyaniline(SnO2-PAn)composite prepared by microemulsion polymerization method. The results show that conductive PAn particles help to improve the contact of between Sn particles in the electrode reaction process and enhance the cycling performance of nano-SnO2.
However, using polyaniline powder as an additive for a Li4Ti5O12 anode material in lithium-ion batteries has not been explored. In this work, Li4Ti5O12-polyaniline composite was synthesized using the in situ polymerisation method. The possibility of using Li4Ti5O12-polyaniline composite as an anode material for lithium ion batteries was examined.
2 Experimental
6.151 g lithium acetate was solved in a certain quantity of ethanol absolute and 10 mL tetrabutyl titanate was added according to the molar ratio of Li to Ti of 4:5 with stirring for 30 min to get a precursor solution of Li4Ti5O12. This solution was added with several droplets of deioned water and kept at 100 ℃ for 4 h to obtain a white or light yellow dry gel. The dry gel was calcinated at 800 ℃ for 20 h in muffer furnace and milled to get Li4Ti5O12 powders.
0.01 mol aniline and ammonium persulfate were solved in 25 mL 1 mol/L HCl. When the ammonium persulfate solution was added to aniline solution, time was recorded. After 3 min, Li4Ti5O12 powders were added to this system according to w(PAn):w(Li4Ti5O12)= 1:19 and the reaction was kept at 30 ℃ for 18 h. After filtering, the product was washed with 0.2 mol/L HCl, 50 mL acetone and 0.2 mol/L HCl, respectively, and immersed in 50 mL 1 mol/L HCl (in which 0.01 mol aniline solved) for 1.5 h. Then the residue was washed with 0.2 mol/L HCl and acetone three times and dyied at 60 ℃ to constant mass in vacuum to get Li4Ti5O12-PAn composite.
Phase identification studies of the samples were carried out by an X-ray diffractometer (XRD; Rigaku D/MAX-gA) with Cu Kα radiation. The infrared (IR) spectra of the samples were conducted on a Fourier transform infrared spectrometer (Nicolet).
A slurry containing 80% (mass fraction) Li4Ti5O12-PAn composite, 10% acetylene black and 10% PVDF (polyvinylidene fluoride) was made using N-methylprrolidinone (NMP) as the solvent. Electrodes with an area of 1 cm2 for the measurements of electrochemical characterization were prepared by coating slurries (about 100 μm in thickness) on copper foils followed by drying in vacuum at 60 ℃ for 12 h. Electrochemical tests were conducted using a conventional coin-type cell, employing lithium foil as a counter electrode and utilizing 1.0 mol/L LiPF6 in ethylene carbonate/dimethyl carbonate (EC/DMC) (with volume ratio of EC to DMC of 1:1) as the electrolyte. The assembly was carried out in an Ar-filled glove box. The electrochemical analyses were carried out with an electrochemical analysis system.
3 Results and discussion
Fig.1 shows the XRD patterns of PAn, Li4Ti5O12 and Li4Ti5O12-PAn. All XRD peaks in Fig.1(a) are in the range of 2θ=10?-30?, indicating that the prepared PAn has a pseudo-orthorhombic crystal structure, in which single-chain of polymers and Cl- is in a way of close packing[16]. XRD peaks in Fig.1(b) agree well with those of the standard JCPDS card No.490207, suggesting that the synthesized sample is spinel Li4Ti5O12. Li4Ti5O12 shares a face centered cubic structure with a space group of 
(a=8.36 ?), in which Li+ is in 8a-site of tetrahedron ,Ti4+ is in 16d-site of octahedron (the molar ratio of Li to Ti is 4:5), while O2- is in sites of 32e [17-18]. There is no peak between 2θ=10?-30? in Fig.1(c), which indicates that PAn in Li4Ti5O12-PAn composite is in amorphous form and the exist of Li4Ti5O12 affects the XRD pattern of PAn significantly. It may be caused by the deposition of PAn on the surface of Li4Ti5O12 particle, which prevents the crystallization of PAn and is very similar to the result of Fusalba[19]. They found that the exist of MoS3 in PAn/MoS3 composite reduces the crystallization of PAn.
Fig.1 XRD patterns of PAn(a), Li4Ti5O12(b) and Li4Ti5O12- PAn (c)
Fig.2 presents the IR spectra of of PAn, Li4Ti5O12 and Li4Ti5O12-PAn. In the IR spectrum (Fig.2(a)) of PAn, four strong characteristic absorption bands appear at 819, 1 131, 1 299 and 3 454 cm-1, are assigned to C—H out- of-plane bending vibration, N=Ar=N mode of vibration, C—N stretching vibration and N—H stretching vibration of two substituted benzenes, respectively. The absorption bands at 1 497 and 1 581 cm-1 are attributed to skeletal vibration of N—Ar—N and N=Ar=N[20]. Fig.2(b) shows the IR spectrum of Li4Ti5O12, and the absorption bands at 676.8 and 457.0 cm-1 present the symmetrical stretching vibration and asymmetrical stretching vibration of Ti—O[21], respectively. In the IR spectrum of Li4Ti5O12-PAn composite (Fig.2(c)), except for the characteristic absorption bands assigned to PAn, there appear peaks at 676.8 and 457.0 cm-1 assigned to Ti-O stretching vibration too, indicating that Li4Ti5O12-PAn composite shows the common characteristics of PAn and Li4Ti5O12 and is the complex of PAn and Li4Ti5O12.
Fig.2 IR spectra of of PAn(a), Li4Ti5O12(b) and Li4Ti5O12- PAn (c)
Fig.3 shows the first discharge curves of Li4Ti5O12- PAn composite and Li4Ti5O12. On the discharge curves of both materials, a long plateau at 1.60 V appears, which corresponds to the normal reversible change of active material Li4Ti5O12[8, 22-23], namely, the active material converts from Li4Ti5O12 to Li7Ti5O12 with the reduction of Ti4+ to Ti3+ of 1 mol. Meanwhile, a short plateau at 0.6-0.7 V appears, which may be associated with the further reduction of the remaining Ti4+ in Li4Ti5O12 toTi3+, suggesting a multi-step restore of Li+ during the discharge period of Li4Ti5O12[24]. The first discharge capacity of Li4Ti5O12-PAn is 191.3 mA?h/g, slightly less than that of Li4Ti5O12. However, the discharge capacities of two materials are to some extent higher than the theoretical specific capacity of the spinel Li4Ti5O12, 175 mA?h/g[25]. The extra capacity must be associated with the second platform at 0.6-0.7 V, suggesting the further reduction of the remaining Ti4+.
Fig.3 First discharge curves of Li4Ti5O12-PAn and Li4Ti5O12 at 0.1C (2.5-0.5 V)
Fig.4 shows the first discharge curves of Li4Ti5O12-PAn at various current rates. From Fig.4, three effects can be found as follows: 1) Cell voltage decreases with the increase of discharge current. It is 1.60 V at 0.1C and drops to about 1.35 V at 2.0C. 2) The discharge capacity of Li4Ti5O12-PAn exhibits a tendency to decrease with the increase of discharge current rate. It is 191.3 mA?h/g at 0.1C and decreases to about 148.9 mA?h/g at 2.0C. 3) With the discharge current rate increasing, the discharge capacity increases in 0.6-0.7 V, which agrees well with the results of Li4Ti5O12/Ag composite[10, 24].
Fig.4 First discharge curves of Li4Ti5O12-PAn at various current rates (2.5-0.5 V)
The cyclabilities of Li4Ti5O12-PAn composite at various current rates were conducted as shown in Fig.5. With the current rate increasing, the discharge capacity decreases. After cycling 80 times, the discharge capacity at 0.1C decreases from 191.3 mA?h/g to 172.0 mA?h/g, and the capacity loss per cycle is 0.13%; while the discharge capacity at 2.0C decreases from148.9 mA?h/g to 76.2 mA?h/g, the capacity loss per cycle is 0.61%. This result shows that small current rate reduces the cell polarization; therefore, the capacity loss decreases and the cycling performance of Li4Ti5O12-PAn composite is improved.
Fig.5 Cyclability of Li4Ti5O12-PAn at various current rates (2.5-0.5 V)
Comparison of cycling performance for Li4Ti5O12- PAn and Li4Ti5O12 anode materials is summarized in Table 1. It is obvious that the discharge capacity of Li4Ti5O12-PAn composite is slightly less than that of Li4Ti5O12 because the ratio of active material Li4Ti5O12 decreases when PAn is added to Li4Ti5O12 to form composite. With the discharge current rate increasing, the cell polarization increases and the discharge capacities of two materials decrease. The capacity loss per cycle after cycling 10 times for Li4Ti5O12-PAn composite is slightly lower than that of Li4Ti5O12.When discharged at 2.0C, the reversible capacity of Li4Ti5O12 is 125.9 mA?h/g and the capacity loss per cycle is 1.57% after cycling 10 times; under the same conditions, the reversible capacity of Li4Ti5O12-PAn is more than 131.6 mA?h/g and the capacity loss per cycle is only 1.16%. Similar to the Li4Ti5O12/Ag composite[10,24], since the electronic conductivity of the pristine Li4Ti5O12 is very low, the conductive PAn additive significantly enhances the surface intercalation reaction and reduces the cell polarization; therefore, the rate performance of the composite is improved.
Table 1 Comparison of cycling performance for Li4Ti5O12-PAn and Li4Ti5O12 anode materials
In order to compare the conductivity of Li4Ti5O12- PAn and Li4Ti5O12, the AC impedance spectroscopy of Li4Ti5O12-PAn and Li4Ti5O12 at ambient temperature was conducted in the frequency range of 10-3-106 Hz as shown in Fig.6. The open-circuit voltage is 1.52 V. A typical semicircle and an inclined line are seen in both curves of Li4Ti5O12-PAn and Li4Ti5O12. The high frequency arc is attributed to the charge transfer reaction at the interface of electrolyte and electrode. The inclined line corresponds to Warburg impedance related to the diffusion of lithium ion in the anode.
Fig.6 AC impedance plots of Li4Ti5O12-PAn and Li4Ti5O12
The conductivity of the specimen is determined by the AC impedance spectroscopy at ambient temperature. According to the formula as follows[24]: σ=d/AR, where σ is the conductivity; R is the resistance; d is the diameter and A is the specific surface area. The conductivities of Li4Ti5O12-PAn and Li4Ti5O12 are 8.6×10-7 S/cm and 4.4×10-7 S/cm, respectively. Since PAn does not enter the spinel structure, the PAn is just coated on the surface of Li4Ti5O12 particle, and the increase of the conductivity in the PAn coated specimen is mainly due to the increase of the electronic conductivity of Li4Ti5O12.
4 Conclusions
1) Li4Ti5O12 powders are prepared by so-gel method using tetrabutyl titanate, lithium acetate and absolute alcohol as starting materials. Li4Ti5O12-polyaniline (Li4Ti5O12-PAn) composite is prepared by in situ polymerization method using aniline, ammonium persulfate and hydrochloricarried as starting materials.
2) The electrical conductivity is enhanced obviously due to the introduction of PAn to Li4Ti5O12. Li4Ti5O12- PAn composite exhibits better high-rate capability and cyclability than Li4Ti5O12. The composite can deliver a specific capacity of 191.3 and 148.9 mA?h/g, only 0.13% and 0.61% of the capacity is lose after being discharged 80 times at 0.1C and 2.0C, respectively.
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Foundation item: Project(20376086) supported by the National Natural Science Foundation of China; Project(2005037700) supported by Postdoctoral Science Foundation of China; Project(07JJ3014) supported by Hunan Provincial Natural Science Foundation of China; Project(07A058) supported by Scientific Research Fund of Hunan Provincial Education Department; Project(2004107) supported by Postdoctoral Science Foundation of Central South University, China
Corresponding author: HE Ze-qiang; Tel: +86-743-8563911; E-mail: csuhzq@163.com
(Edited by ZHAO Jun)
