Journal of Nanomaterials

Volume 2012 (2012), Article ID 394089, 8 pages

doi:10.1155/2012/394089

Research Article

Lithium Ion Storage Characteristics of Mechanically Fractured Titanate Nanotubes

Jeongeun Kim,¹ Minyong Eom,² Yongsub Yoon,¹ and Dongwook Shin1,2

¹Department of Materials Science and Engineering, Hanyang University, 222 Wangsimni-ro, Seongdong-gu, Seoul 133-791, Republic of Korea

²Department of Fuel Cells and Hydrogen Technology, Hanyang University, 222 Wangsimni-ro, Seongdong-gu, Seoul 133-791, Republic of Korea

Received 8 February 2012; Revised 30 July 2012; Accepted 30 July 2012

Academic Editor: Mauro Coelho dos Santos

Copyright © 2012 Jeongeun Kim 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.

The effect of mechanical milling on the formation of short titanate nanotube and structural change induced is investigated. Mechanical milling produces the short nanotubes with the length of 30–160 nm. The lithium ion intercalation characteristics of the obtained short titanate nanotube were studied to verify the effect of the newly formed cross-sections of nanotubes. It was found that the protonated titanate nanotubes maintained long shapes until 30 min of mechanical milling and were transformed into agglomerated nanosheets and finally anatase granules depending on the treatment duration. Through galvanostatic investigation, the nanotubes with milling of 15 min exhibited the highest discharge capacity of 336 mAh·g⁻¹ in first cycle, 12.4% larger than pristine.

1. Introduction

Nanostructured electrodes fabricated from nanotubes, nanowires, or nanofibers have shown unique rate capability for lithium ion batteries since the distance Li⁺ ions penetrate is as small as several nanometers in the radius direction which is significantly smaller than that in the usual power. As a result, there is tremendous research interest in the development of nanostructured Li-ion battery electrode with high capacity and excellent cycling stability [1–6].

Many researchers have recently prepared titanate nanotubes and developed their electrochemical properties by precise control over their morphology for various applications. It has been found that the properties of these nanomaterials depend strongly on their size and shape. Therefore, it is important to control their size and the morphology to make use of them in suitable applications. Especially much attention has been paid to nanotubes for electrochemical lithium storage due to their open, mesoporous structure, large specific surface, efficient transport of lithium ions, and impressive ion-exchange properties, which result in a high value of charge/discharge capacity [7–12].

Li et al. and Zhou et al. reported on the effect of the titanate morphology produced by changing process parameters on the battery performance [13–16]. Bavykin et al. reported the rate of ion exchange along length of titanate nanotubes [17]. For the shortest nanotubes (having an average length ca. 50 nm), the characteristic time of the ion exchange was shorter than that for long nanotubes, suggesting that the diffusion of ions along the length of the tube could be the rate-limiting step. Although this finding was pioneering, they did not investigate the effect of titanate nanotube length on the electrochemical characteristics as an anode material for lithium battery. It is our main objective to carry out the basic estimation on the battery performance of titanate nanotubes with various lengths and verify the possibility of improving the poor cyclability of titanate nanotubes, by changing the nanotube length.

For an anode for lithium ion battery, it was confirmed that, at the first discharge stage, lithium intercalation occurred at inner and outer surface of nanotube. Some of these intercalated lithium ions could not be extracted from deep interlayer sites on inner surface of the nanotube and, hence, electrochemical reactions occur actively only at the both end of nanotubes [15, 16, 18]. In the interests of large surface area for electrochemical reaction sites of LixTiO₂ and short nanochannel for easy and fast transport of Li ion for lithium intercalation, we synthesized the short length of nanotubes by low-energy mechanical milling from the hydrated titanate nanotubes synthesized via alkaline hydrothermal treatment of TiO₂ and subsequent acid treatment [19, 20]. To verify the effect of mechanical milling treatment on titanate nanotube for battery performance, the length of the titanate nanotube was controlled by various milling condition, and basic charging-discharging behavior of nanotubes as anode was estimated.

2. Experimental Methods

Titanate nanotubes were prepared by alkali hydrothermal method. Commercial titanium oxide powder (P25, Degussa AG) was used as a precursor to synthesize titanate nanotubes (TNTs). 4 g of the TiO₂ precursor and 180 mL of 10 M NaOH (98%, SAMCHUN) aqueous solution were mixed under stirring for 3 h. The suspension was poured into a Teflon vessel and placed in autoclave for hydrothermal treatment at 130°C for 24 h and cooled to room temperature. The synthesized solution was washed for 24 h with HCl (35%, DAEJUNG) acid solutions in pH 1 and then washed continuously with distilled waters to pH 7 to remove to extract sodium. The samples were filtered and dried at 60°C for 24 h. Titanate nanotubes were treated in a mechanical ball milling using identical milling parameters. The milling performed in air using a Fritsch planetary ball mill, with balls made of zirconium dioxide. The powder-to-ball weight ratio was chosen to be 1 (powder): 15 (ball), while the milling time was varied from 15 to 60 min under the rotational speed of 100 rpm.

The morphology and structural changes of titanate nanotubes with various milling conditions were characterized using BET (Surface Characterizing Analyzer, ASAP2010 & TriStar3000, USA), (X-ray diffraction XRD, Rigaku d-max 3000, Japan), (High Resolution Transmission Electron Microscopy TEM, JEM-2100F, Japan), and (Field Emission Scanning Electron Microscopy FE-SEM, Hitachi S-4800, Japan).

(Thermogravimetric-differential thermal analysis TG-DTA, TGA7, PERKIN ELMER) was performed with a temperature range of room temperature to 500°C.

For fabrication of electrodes, the active materials prepared with the mixture of carbon black, and isopropyl alcohol, and the obtained titanate nanotubes were coated on copper foil and, then, dried at 120°C for 12 hours to remove the solvents. The tests were performed on a coin-type cell assembled with as-prepared electrode, lithium metal as the counter, separator, and an electrolyte. The electrolyte solution was LiPF₆ dissolved in a mixture of EC (ethylene carbonate) and (dimethyl carbonate DMC) with the volume ration of 1 : 1.

Electrochemical properties measuring were using TOSCAT cell test instrument (Toyo system, Japan). Charge and discharge were conducted between 3 and 1 V versus Li⁺ reference electrode at 0.1 C rate. Cyclic voltammogram was measured from 3 and 1 V range at 0.2 mV·s⁻¹, using electrochemical interface (SI 1287, UK).

3. Results and Discussion

Figure 1 shows the XRD patterns of the as-prepared titanate nanotubes and the mechanically milled in condition of 100 rpm for 15, 30, 45, and 60 min. All the powders exhibited characteristic peaks at around 2θ = 10°, 24°, and 28°, which are assigned to the diffraction of H₂Ti₂O₅·H₂O (JCPDS, Card 47-0124) with peak broadening by nanometer size [20–23]. It was known that the nanotubes showed weak diffraction lines because of their tubular structure and poor crystallinity [24]. The gradual changes in the major diffraction peaks suggest that the mechanical milling affected both the length and the structure of nanotubes. The intensities of main peaks at 2θ = 10° and 28° of titanate nanotubes were slightly decreased and broadened with increasing milling time, which suggests that nanotube structure was gradually distorted along with shortening by mechanical milling process. Unlike main peaks of nanotube, the peaks at 2θ = 24° and 48.5° were maintained under whole milling conditions. Plodinec et al. confirmed that during the mechanical milling treatment the phase transitions from titanate nanotubes to anatase phase and finally rutile phase were observed since the high-energy ball milling generated defects, and it influenced the composition and the stoichiometry [25]. Similar phase change was observed in this work; nanotube structure was distorted and converted into anatase phase gradually. After milling for 60 min, most of nanotubes seemed to collapse into anatase crystalline granules.

Figure 1: XRD patterns of the as-prepared titanate nanotubes and the produce of mechanical milling.

The variation of surface area of the mechanically milled product is summarized in Table 1. The surface area increases with milling and reached the highest value of 550 m²·g⁻¹ at 15 min and then decreases with an increase in the milling time. This is believed to be due to the agglomeration of fractured nanotubes and the anatase granules. At 60 min of milling the surface area was decreased to 273 m²·g⁻¹, suggesting that the highly agglomerated anatase granules were formed as supported from XRD data in Figure 1.

Table 1: Surface area of the starting material, the as-prepared, and mechanically milled.

Condition of milling (min)
P25
0
15
30
60

Surface area, SBET (m²·g⁻¹)
55–60
500
550
513
273

Figures 2 and 3 show the HRTEM and FESEM images of the titanate nanotubes. As-prepared titanate nanotubes were long and slim tubular shape, whose diameter was around 10 nm and length was several hundred nanometers. HRTEM image in as-prepared protonated titanate nanotubes shows that the synthesized nanotubes have 4-5 layers with open ends. The nanotubes were slightly shortened by milling for 15 min to approximately ~100 nm in length and milling for 30 min to 30–100 nm. However, the number of wall layers and the size of interspacing remained similar to those of the as-prepared long titanate nanotubes. After 45 min, the particle type granules were observed that the titanate nanotubes were fractured and transformed to anatase particles with excessive milling treatment. XRD data in Figure 1 support that short titanate nanotubes maintained the H₂Ti₂O₅·H₂O structure up to 30 min of milling. Figure 3 shows that the partial change of powder morphology took place with milling treatment. It is clear that the degree of agglomeration is slightly intensified with milling time. After 60 min, tubular type morphology is not shown as TEM image, and anatase granules were agglomerated by increased treatment duration.

(a)

(b)

(c)

(d)

(e)

Figure 2: TEM images of (a) the as-prepared protonated titanate nanotubes, and the titanate nanotubes with mechanical milling in condition of (b) 15, (c) 30, (d) 45, and (e) 60 minutes at 100 rpm.

(a)

(b)

(c)

(d)

(e)

Figure 3: SEM images of (a) the as-prepared protonated titanate nanotubes, and the titanate nanotubes with mechanical milling in condition of (b) 15, (c) 30, (d) 45, and (e) 60 minutes at 100 rpm.

Figure 4 shows the initial charge/discharge behavior of lithium intercalation in the titanate nanotubes before and after milling treatments at current rate of 10 mA·g⁻¹ between 1.0 V and 3.0 V. The initial discharge capacities were varied from 335 mAh·g⁻¹ to 210 mAh·g⁻¹, and initial charge capacities were varied from 280 mAh·g⁻¹ to 114 mAh·g⁻¹ depending on milling duration. As-prepared titanate nanotubes exhibited the initial charge and discharge capacity of 219 mAh·g⁻¹ and 299 mAh·g⁻¹, respectively, with a reversible efficiency of 73.2%. However, charge and discharge capacities were increased to 280 mAh·g⁻¹ and 336 mAh·g⁻¹ for milling of 15 min with a reversible efficiency of 83.3%. After milling of 15 min, the capacities rapidly decreased with increasing milling time. One can see that morphological and structural change, controlling the length of titanate nanotubes, seems to have a noticeable effect on the cell performance. At the initial stage of milling treatment, long nanotubes were fractured into short nanotube that had the highest value of surface area for the absorption of Li ion and short nanochannel for easy and fast transfer of Li⁺ for lithium intercalation. Further milling treatment, however, starts to produce nanosheets with lower intercalation capability. Due to the increase of less active phases, even though nanotubes are shorten further, the charge/discharge capacities decrease. After 30 min of milling, the nanotubes transformed to anatase granular structure, and consequently a distinguishing characteristic of nanotubes was disappeared.

Figure 4: Initial charge/discharge profile of titanate nanotubes with the milling condition of 0, 15, 30, 45 and 60 minutes at a current rate of 10 mA·g⁻¹ between 1.0 and 3.0 V.

Figure 5 shows the cyclic voltammograms of the samples at a scan rate of 0.2 mV·s⁻¹. In the first cycle, there is only a pair of broad redox peaks for nanotubes as prepared and milling 13 and 30 min. The pseudocapacitive behavior of this peak is explained in terms of the interaction taking place on the nanosheet surface, hence curved one. The TiO₂ nanotubes hold the curved nanosheet-like morphology with thin-wall structure and high specific surface area.

(a)

(b)

(c)

(d)

(e)

Figure 5: Cyclic voltammogram plots of TiO₂ nanotube electrodes (a) and with mechanical milling in condition of (b) 15, (c) 30, (d) 45, and (e) 60 minutes at 0.2 mV·s⁻¹.

In the case of the nanotubes with milling 45 min, a pair of shoulder redox peaks near the larger broad redox peaks appears at 1.75 and 1.95 V (versus Li⁺/Li, depending on the scan rate), which is characteristic for lithium insertion into anatase lattice, revealing the possible phase transition from titanate to anatase. Obviously, the pair of shoulder redox peaks related to lithium insertion/extraction in anatase becomes larger with increasing milling time, accompanied by a decrease of the broad redox peaks and a structural transformation from titanate to anatase [26].

Figure 6 shows the galvanostatic charge/discharge recyclability for the titanate nanotube and the materials produced by milling treatments. The cutoff potentials for the charge/discharge were set to be 1.0 V to 3.0 V versus Li⁺/Li. All samples exhibited an obvious drop of discharge capacity during first several cycles that may be due to the formation of LiO₂ or LiOH by left remained water in nanotubes on the surface of electrode [27]. The electrochemical discharge capacities of titanate nanotubes with milling decreased gradually and showed poor cycle stability for lithium insertion and extraction compared to nanotube. In spite of highest value of initial charge and discharge capacities, the short titanate nanotubes produced by milling contain defects in composition and structure, and these defects cause irreversible capacities accumulating every cycles.

Figure 6: Charging-discharging curves of the coin cell composed of titanate nanotubes//1 M LiPF₆-EC/DEC//Li metal at a current rate of 10 mAh·g⁻¹ between 1 V and 3 V. The titanate nanotubes with the millinging condition of 0, 15, 30, and 60 minutes were used as an anode-active materials.

4. Conclusion

Titanate nanotubes were synthesized by the hydrothermal method and treated in a high-energy ball milling in various duration conditions. The structure of nanotubes was H₂Ti₂O₅·H₂O with inner and outer diameter of 5 nm and 10 nm. Increasing milling duration, the titanate nanotubes were fractured into short length of nanotubes, and finally transformed to anatase structure. The 15 min sample shows that high initial charge and discharge capacities of 280 mAh·g⁻¹ and 336 mAh·g⁻¹ observed in the titanate nanotube, which shows an effect of shorted titanate nanotubes. The length of nanotubes had an effect on cell performance due to high specific surface area for absorption of Li ion and short nanochannel for easy and fast transfer of Li⁺ for lithium intercalation; however, the cyclic stability was not greatly improved because of structural and compositional defects caused by high-energy ball milling. Further study is required the synthesis of short nanotube without structural change and defect, which can solve the problems of low initial capacity and poor cyclability of titanate nanotubes.

Acknowledgments

This research was supported by a grant from the Fundamental R&D Program for Core Technology of Materials funded by the Korean Ministry of Knowledge Economy (Grant no. 10037233).

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