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Volume 2018 (2018), Article ID 4725328, 7 pages
https://doi.org/10.1155/2018/4725328

Research Article

Flexible Freestanding Carbon Nanofiber-Embedded TiO₂ Nanoparticles as Anode Material for Sodium-Ion Batteries

Xuzi Zhang,¹ Zhihong Chen,² Lingling Shui,¹ Chaoqun Shang,¹ Hua Liao,³ Ming Li,³ Xin Wang,1,4 and Guofu Zhou1,4

¹National Center for International Research on Green Optoelectronics, South China Normal University, Guangzhou, China
²Shenyang Institute of Automation, Chinese Academy of Sciences, Guangzhou, China
³Institute of Solar Energy, Yunnan Normal University, Kunming, China
⁴International Academy of Optoelectronics at Zhaoqing, South China Normal University, Guangdong, China

Correspondence should be addressed to Chaoqun Shang; chaoqun.shang@ecs-scnu.org and Xin Wang; wangxin@scnu.edu.cn

Received 31 May 2018; Accepted 30 July 2018; Published 4 November 2018

Academic Editor: Huaiyu Shao

Copyright © 2018 Xuzi Zhang et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

Sodium-ion batteries (SIBs), owning to the low cost, abundant resources, and similar physicochemical properties with lithium-ion batteries (LIBs), have earned much attention for large-scale energy storage systems. In this article, we successfully synthesize flexible freestanding carbon nanofiber-embedded TiO₂ nanoparticles (CNF-TiO₂) and then apply it directly as anode in SIBs without binder or current collector. Taking the advantage of flexible CNF and high structural stability, this anode exhibits high reversible capacity of 614 mAh·g⁻¹ (0.27 mAh·cm⁻²) after almost 400 cycles and excellent capacity retention ability of ~100%

1. Introduction

Sodium-ion batteries (SIBs) have earned much attention as a candidate substitution for lithium-ion batteries (LIBs) in the area of large-scale energy storage [1, 2], which is ascribed to the earth’s abundance of sodium resource and similar physicochemical properties with LIBs [3–5]. Until now, many efforts have been made to solve the slow sodiation/desodiation kinetics and large-volume expansion caused by a large radius of Na⁺ (1.02 Å versus 0.76 Å of Li⁺) [6–8]. Furthermore, the capacity and cycling stability also need to be improved to satisfy the practical application. It is essential to select and design proper anode materials for SIBs to realize fast Na⁺ insertion/extraction with high capacity and cycling stability [9, 10].

Among numerous anode material candidates, TiO₂ with anatase phase has been explored as a promising anode material for SIBs with low cost, abundance, environmental benignity, and excellent structural stability [11–13]. However, the undesirable electrical conductivity and sluggish ionic diffusivity restrict its further applications [14]. Many efforts have been cost to improve the ion/electron transportation for SIBs. Zhu and coworkers [15] synthesized TiO₂ nanoparticles coated by mutiwalled carbon nanotubes and carbon nanorods as anode, exhibiting excellent rate capability and cycling stability. He and coworkers [16] prepared a hierarchical rod-in-tube structure TiO₂ modified with a conducive carbon layer as anode, which delivered fast ion diffusion and high conductivity. Therefore, the efficient strategy to enhance the electrochemical performance is nanosizing TiO₂ and then incorporating with the conductive matrix [16–22]. Despite the progresses, the rational design nanostructure of TiO₂-based anode is still of great demand.

Herein, we proposed freestanding flexible winkled carbon nanofiber-embedded anatase TiO₂ nanoparticles (CNF-TiO₂) as anode of SIBs directly without binder and current collector, which can not only increase the energy density but also explore the potential application in flexible devices. The long-range continuous carbon nanofibers can improve the conductivity of nanosized anatase TiO₂, and the thin fibers can shorten the diffusion path of Na⁺, which can promote the electrochemical kinetics in Na⁺ insertion/extraction. The freestanding flexible 3D carbon structure and embedded TiO₂ nanoparticles can improve structural stability to alleviate the volume change during Na⁺ insertion/extraction. In addition, the rough surface of CNFs increases the electrode-electrolyte contact points and lowers the charge transfer resistance. High specific capacity of 614 mAh·g⁻¹ (0.27 mAh·cm⁻²) was obtained after almost 400 cycles with capacity retention of ~100%, confirming the potential of CNF-TiO₂ as anode for SIBs.

2. Experimental Section

2.1. Synthesis of the Freestanding CNF-TiO₂

The electrospinning precursor solution was prepared firstly by dissolving 1.48 g polyacrylonitrile (PAN, , Sigma-Aldrich) in 18 ml N,N-dimethylformamide (DMF) under magnetic stirring overnight. Then, 2.5 ml tetrabutyl titanate (Ti(OC₄H₉)₄) was added into this solution and stirring was continued for 10 min to obtain homogeneous white turbid solution. The distance between the needle and Al foil was 15 cm, and the voltage was maintained at 25 kV. Then the obtained precursor nanofibers were stabilized at 280°C for 2 h with a heating rate of 5°C·min⁻¹ and carbonized at 700°C with 1°C·min⁻¹ for 2 h under argon atmosphere.

2.2. Structure Characterizations

The morphologies and size of CNF/TiO₂ were characterized by scanning electron microscopy (SEM, ZEISS Ultra 55). Transmission electron microscopy (TEM) and EDS mapping were both carried out by JEM-2100 HR. The crystalline property of CNF-TiO₂ was recorded by Bruker D8 Advance. The thermal gravity analysis TG test was performed to evaluate the content of TiO₂ by Netzsch STA 449. The 250Xi X-ray photoelectron spectroscope (XPS) was obtained from ESCALAB.

2.3. Electrochemical Tests

The CR2016-type coin cells were assembled with sodium metal as the reference electrode, glass fiber membrane as the separator, and the as-prepared CNF-TiO₂ directly as the anode. The above procedures were all carried out in an Ar-filled glove box (, ). The electrolyte was 1 M NaClO₄ in propylene carbonate (PC)/ethylene carbonate (EC) (, in volume). The cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) results were obtained from an electrochemical workstation (CHI660E, Shanghai Chen Hua Instruments Ltd). Also, the galvanostatic discharge-charge tests were conducted in a Neware battery testing system.

3. Results and Discussion

The structure and morphology of CNF-TiO₂ are detected by XRD, TG, XPS, SEM, and TEM. As shown in Figure 1(a), all the diffraction peaks matched well with anatase TiO₂ (JCPDS number 021-1272), which confirms that the pyrolysis temperature is appropriate to gain high-purity anatase TiO₂. Furthermore, the slightly weak intensity of these diffraction peaks suggests that the TiO₂ nanoparticles were well embedded in the carbon nanofibers. In the thermogravimetry measurement (Figure 1(b)) of CNF-TiO₂, the content of TiO₂ is 26.2%. The Ti in CNF-TiO₂ is clarified by X-ray photoelectron spectroscopy (XPS) as shown in Figure 1(c), which indicates two peaks of 464.6 eV and 458.7 eV, corresponding to the orbits of 2p 3/2 and 2p 1/2 of Ti⁴⁺, respectively. The Ti 2p XPS result also confirms the formation of anatase TiO₂.

(a)

(b)

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Figure 1: (a) The XRD pattern of CNF-TiO₂ after pyrolysis at 700°C; (b) TG pattern of CNF-TiO₂ under air atmosphere; (c) XPS of Ti 2p in CNF-TiO₂.

Figures 2(a)–2(f) perform the morphologies of CNF-TiO₂. SEM images (Figures 2(a)–2(c)) show an extremely rough surface of the as-synthesized nanofibers with diameter of ~300 nm. Many wrinkles appear after 700°C pyrolysis treatment for the crystallization of TiO₂ nanoparticles and decomposition of the polymer fibers, which may provide active sites for Na⁺ insertion/extraction. In addition, the long-range continuous carbon nanofiber matrix with high conductivity will lead to fast electron transmission. As for the TEM images with different magnification (Figures 2(d)–2(f)), the well-distributed TiO₂ nanoparticles can be clearly observed with sizes between 100 nm and 200 nm and they are all coated with amorphous carbon. A lattice spacing of 0.363 nm, corresponding to (101) planes of anatase TiO₂, can be clearly detected in the high-resolution TEM image (Figure 2(f)), which means the high degree of crystallinity of anatase TiO₂. The TiO₂ larger lattice spacing of 0.363 nm than 0.102 nm of Na⁺ and the specific space group of I4₁/amd (, and ) can ensure the fast insertion/extraction of Na⁺ [23, 24], in which Na⁺ is inserted/extracted in the interspace of anatase TiO₂ [23]. Furthermore, it can stabilize the structure of CNF-TiO₂ cooperated with amorphous carbon through enduring the volume change in the battery reaction.

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(b)

(c)

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Figure 2: SEM images (a–c), TEM images (d–f), and EDS mapping (g) of CNF-TiO₂.

The electrochemical performance of CNF-TiO₂ anode for SIBs is investigated by cyclic voltammetry (CV) between 0.01 V and 3 V with a scan rate of 0.1 mV·s⁻¹ and galvanostatic charge-discharge techniques at 200 mA·g⁻¹. As depicted in Figure 3(a), a strong cathodic peak between 0 and 0.5 V appears in the first cycle of SIB and disappears in the following four cycles, which demonstrates the decomposition of electrolyte and the formation of solid electrolyte interphase (SEI) film. The benign overlapped CV curves of the next four scans indicate excellent cycle stability and reversibility for Na⁺ insertion/extraction. Figure 3(b) shows the charge/discharge curves of CNF-TiO₂ as anode for SIBs with constant current of 200 mA·g⁻¹. In the initial cycle, there exists a large irreversible capacity compared to the following curves, which is in agreement with the CV tests. The charge/discharge curves without obvious plateaus demonstrate the fluent insertion/extraction of Na⁺ into the amorphous carbon and crystalline TiO₂ lattice. The initial discharge capacity is 792 mAh·g⁻¹ (0.35 mAh·cm⁻²) with a coulombic efficiency of 35.5%, and the discharge capacities increase slightly during the subsequent cycles, showing the continuous reduced resistance of CNF-TiO₂ by the activation of this material, which is also confirmed in electrochemical impedance spectroscopy (EIS, Figure 3(d)). The EIS results show the slight decrease in charge transfer resistance before 10 cycles and then a gradual increase until 80 cycles, which is the consequence of activation and slight structural damage of CNF-TiO₂, respectively.

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Figure 3: (a) CV tests at 0.1 mV·s⁻¹. (b) Galvanostatic charge-discharge curves of CNF-TiO₂ recorded at 200 mA·g⁻¹; (c) rate performance of CNF-TiO₂; (d) EIS of CNF-TiO₂ before and after cycles; (e) cycling stability of CNF-TiO₂ as anode for SIBs at 200 mA·g⁻¹.

The rate performance of CNF-TiO₂ is further investigated at various constant currents from 100 mA·g⁻¹ to 5000 mA·g⁻¹. As shown in Figure 3(c), the capacity can still retain 378 mAh·g⁻¹, 309 mAh·g⁻¹, and 133 mAh·g⁻¹ at the current densities of 1000 mA·g⁻¹, 2000 mA·g⁻¹, and 5000 mA·g⁻¹, indicating the rapid process of the insertion/extraction of Na⁺. Moreover, when the current density recovers to 100 mA·g⁻¹, the capacities can retain to the initial level, showing the outstanding rate performance of CNF-TiO₂ as anode for SIB. CNF-TiO₂ also exhibits remarkable long-term cycling stability (Figure 3(e)). It can deliver a high initial capacity of 792 mAh·g⁻¹ with a coulombic efficiency of 35.5% and stability at 614 mAh·g⁻¹ after almost 400 cycles, indicating the excellent cycling performance and structural stability of CNF-TiO₂ anode. On the one hand, the large length-to-volume ratio of CNFs-TiO₂ provides more active sites for Na ion adsorption on the surface of 1D nanofibers, which offers additional capacity contribution. On the other hand, the specific capacity of CNFs-TiO₂ is based on the mass of TiO₂, while the carbon substrate may contribute partial capacity. It should be noted that the capacity increases during the initial cycles, which might be attributed to the active process owing to the 3D interconnected nanostructure of CNF-TiO₂ [16].

To further unravel the electrochemical kinetic properties of CNF-TiO₂ as anode in SIBs, CV tests at different scan rates from 0.1 mV·s⁻¹ to 1 mV·s⁻¹ are performed in Figure 4(a). All the CV cycles have a similar shape of broad peaks for Na⁺ insertion/extraction. Also, the small peak shift with different scan rates indicates the smaller polarization of CNF-TiO₂. The peak current () of curves can be separated into two mechanism parts: diffusion-controlled and surface-controlled, which corresponds to battery and capacitive reaction, respectively.

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Figure 4: (a) CV curves of CNF-TiO₂ at different scan rates from 0.1 mV·s⁻¹ to 1 mV·s⁻¹. (b) The relationship between peak current (i) and scan rates (v). (c) The contribution of capacitive (red) and battery (blank) reaction at 0.5 mV·s⁻¹. (d) The ratio of capacitive and battery contribution at different scan rates.

In order to figure out the contribution of each part, the equation of [25, 26] linked peak current (, mA) and scan rate (, mV·s⁻¹) is performed to qualitatively analyze the kinetics, which can also express as log ·log v. and are constants which are obtained from the experiments. The value is represented by the slope of log plots. There are two limit cases: that means a diffusion-controlled mechanism (battery) and that represents a surface-controlled process (capacitive). As shown in Figure 4(b), the cathodic peaks show the estimated value of 0.895 and anodic peaks of 0.849 from 0.1 mV·s⁻¹ to 1 mV·s⁻¹, which means the electrochemical kinetic of CNF-TiO₂ as anode is the combined mechanism of diffusion control and surface control (dominant).

Furthermore, the capacitive contribution and battery contribution can be separately quantitatively analyzed by the equation [20], where is the current at a fixed voltage with different scan rates, and and originated from the contribution of surface-controlled and diffusion-controlled reaction, respectively. In order to easily calculate, this formula can be transformed to . Then, and can be obtained from the fitting plot of . Figure 4(c) shows that the current is derived from two parts with the obvious red shadow area and blank space representing capacitive and battery reaction, respectively, which indicates that the contribution of capacitive effect is 54.3%. Figure 4(d) exhibits the capacity contribution increasing with the rising scan rates, 46.2% (0.1 mV·s⁻¹), 53% (0.3 mV·s⁻¹), 54.3% (0.5 mV·s⁻¹), 65.4% (0.7 mV·s⁻¹), and 68.4% (0.9 mV·s⁻¹). These capacitive contributions reveal that CNF-TiO₂ as anode can shorten the electron transfer path and decrease the barrier of Na⁺ insertion/extraction.

4. Conclusion

In summary, this flexible freestanding CNF-TiO₂ can be successfully synthesized by a facile electrospinning method followed by pyrolysis treatment at 700°C. This material as anode exhibits high specific reversible capacity of 614 mAh·g⁻¹ (0.27 mAh·cm⁻²), excellent rate performance, and long-cycle stability at 200 mA·g⁻¹, which can be ascribed to the long-range continuous conductive carbon nanofibers and TiO₂ nanoparticles with excellent structural stability and larger lattice of 0.363 nm than the radius of Na⁺. After almost 400 cycles, the capacity retention keeps ~100%, which indicates the high reversible performance and excellent tolerance of volume change in the process of Na⁺ insertion/extraction.

Data Availability

The data used to support the findings of this study are included within the article.

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

The authors acknowledge the financial support from the National Natural Science Foundation of China Program (no. 51602111), Cultivation project of National Engineering and Technology Center (2017B090903008), Xijiang R&D Team (Xin Wang), Guangdong Provincial Grant (2015A030310196 and 2017A050506009), Special Fund Project of Science and Technology Application in Guangdong (2017B020240002), and 111 project.

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