Synthesis of Nanocobalt Powders for an Anode Material of Lithium-Ion Batteries by Chemical Reduction and Carbon Coating

Hong, Seong-Hyeon; Jin, Yeong-Mi; Kim, Kyung Tae; Ahn, Cheol-Woo; Park, Dong-Su; Song, Myoung Youp

doi:https://doi.org/10.1155/2014/378103

Journal of Nanomaterials

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Nanomaterial Synthesis, Characterization, and Application

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Volume 2014 | Article ID 378103 | https://doi.org/10.1155/2014/378103

Synthesis of Nanocobalt Powders for an Anode Material of Lithium-Ion Batteries by Chemical Reduction and Carbon Coating

Seong-Hyeon Hong,¹Yeong-Mi Jin,²Kyung Tae Kim,¹Cheol-Woo Ahn,³Dong-Su Park,³and Myoung Youp Song⁴

Academic Editor: Necdet Aslan

Received25 Oct 2013

Revised30 Mar 2014

Accepted01 Apr 2014

Published19 May 2014

Abstract

Nanosized Co powders were prepared by a chemical reduction method with and without CTAB (cetyltrimethylammonium bromide, ) and carbon-coating heat treatment at 700°C for 1 h, and the electrochemical properties of the prepared nanosized Co powders were examined to evaluate their suitability as an anode material of Li-ion batteries. Nanosized amorphous Co-based powders could be synthesized by a chemical reduction method in which a reducing agent is added to a Co ion-dissolved aqueous solution. When the prepared nanosized Co-based powders were subjected to carbon-coating heat treatment at 700°C for 1 h, the amorphous phase was crystallized, and a Co single phase could be obtained. The Co-based powder prepared by chemical reduction with CTAB and carbon-coating heat treatment had a smaller first discharge capacity (about 557 mAh/g) than the Co-based powder prepared by chemical reduction without CTAB and carbon-coating heat treatment (about 628 mAh/g). However, the former had a better cycling performance than the latter from the third cycle. The carbon-coated layers are believed to have led to quite good cycling performances of the prepared Co-based powders from the third cycle.

1. Introduction

There is much interest in several different types of lithium-based rechargeable batteries [1–9], due to the expectation of high specific energies and energy densities. The conventional lithium-ion batteries use carbon-based materials as anodes [10–12], but their theoretical capacity of 372 mAh/g is not sufficient. Therefore, the development of new anode materials with high capacity is needed.

Much work has been conducted on the subject of electrodes using nanosized materials since nanosized powders exhibit good electrochemical performance. Nanosized powder can be synthesized by various methods, such as sol-gel [13], solvothermal [14], spray conversion [15], and pulsed wire evaporation (PWE) methods [16].

Kim et al. [17] synthesized nanosized Co powder by a pulsed wire evaporation method as an anode material for lithium batteries. The Li/Co cell fabricated with the powder showed a plateau potential of 0.7 V and a capacity of 440 mAh/g at the first discharge, and a reversible capacity of about 280 mAh/g after 30 cycles.

An ordered mesoporous Sn-C composite with Sn nanoparticles confined in carbon nanorods was prepared by Chen et al. [18]. This composite delivered a reversible lithium storage capacity of 554 mAh/g at the 200th cycle as an anode material of Li-ion batteries.

Cobalt composites are potential candidates for use as an anode material. Examples are Co-O [19], Co-C [20, 21], Co-Sb [22], Co-Sn [23, 24], and Co-B [25] composites.

Yue et al. [21] synthesized a novel C/Co composite with Co nanoparticles embedded in carbon matrix by the pyrolysis of polymeric cobalt phthalocyanine (PcCo) at 700°C in argon atmosphere. They reported that the C/Co electrode had a reversible capacity of over 600 mAh/g at a current of 50 mAh/g after 40 cycles and showed better rate capability and less hysteresis in comparison with carbon not containing Co.

He et al. [24] performed hydrothermal synthesis and examined the electrochemical properties of nanosized Co-Sn alloy anodes for lithium-ion batteries. They reported that prolonging the dwelling time at the same hydrothermal temperature could increase the content of Sn oxides, which would lead to a high initial irreversible capacity loss, but better cycling stability, owing to the buffer effect of the irreversible product Li₂O.

Yiping et al. [25] produced Co-B fine particles by the chemical reduction of aqueous solutions of cobalt chloride with sodium borohydride. The particle size was in the range of 20–100 nm. Ultrafine Co_74.4B_25.6 amorphous powder was prepared by Yuan et al. [26] with chemical reduction. The as-prepared sample was formed by many interconnected fine particles with sizes smaller than 100 nm.

Co-based powders were prepared via the chemical reduction method by several researchers. Lu et al. [27] reduced cobalt (II) by chemical reduction. They added sodium borohydride at a controlled rate, with the concentration of NaOH varied in the reducing solution. The synthesized particle size was about 20–100 nm.

Ahn [28] reported that nanosized anode materials had high discharge capacities but showed poor cycling performances. Carbon coating is thought to improve cycling performances of anode materials by preventing the formation of SEI (solid electrolyte interphase) layers between anode materials and electrolyte.

In this study, nanosized Co powders were prepared by a chemical reduction method with and without CTAB (cetyltrimethylammonium bromide, C₁₉H₄₂BrN) and carbon-coating heat treatment at 700°C. Then, the electrochemical properties of the prepared nanosized Co powders were examined to evaluate their suitability as an anode material for Li-ion batteries.

2. Experimental Details

In order to synthesize nanosized Co-based powders, the materials listed in Table 1 were used.

Figure 1 shows a schematic of the apparatus used for chemical reduction. CTAB is a cationic surfactant (surface active agent) and was added since its addition was expected to facilitate pore formation. CTAB-added Co powders were synthesized as follows. 5.94 g of cobalt (II) chloride hexahydrate (CoCl₂·6H₂O) and 2.28 g of CTAB were dissolved by stirring in 250 cc of distilled water, which was purged sufficiently with high-purity nitrogen. 9.46 g of a reducing agent granular sodium borohydride was also dissolved by stirring in 250 cc of distilled water, which was also purged sufficiently with high-purity nitrogen. Then, the reducing agent solution was added slowly to the solution containing the solutes in order to prevent abrupt reaction due to CTAB, which can cause boiling over. During this process, nitrogen was purged continuously. After the reaction was completed, the solution was filtered and washed by distilled water and ethanol to prevent oxidation. The prepared powder was then dried.

Co powders without CTAB addition were synthesized as follows. 11.88 g of cobalt (II) chloride hexahydrate (CoCl₂·6H₂O) and 18.92 g of granular sodium borohydride reducing agent were dissolved separately by stirring in 500 cc of distilled water, which was purged sufficiently with high-purity nitrogen. Then, the reducing agent solution was added to the solute-containing solution at a rate of about 500 cc/min. During this process, nitrogen was purged continuously. After the reaction was completed, the solution was filtered and washed by distilled water and ethanol to prevent oxidation, and the prepared powder was dried.

TGA (thermogravimetric analysis) with an SDT2960 (TA Instruments, USA) and DTA (differential thermal analysis) with an STA409pc (Netzsch, Germany) were performed for the synthesized samples by increasing the temperature to 1000°C at a heating rate of 10°C/min in an Ar atmosphere. The sensitivity of the balance was 0.1 g.

Then the powder synthesized by the chemical reduction method was carbon-coated in a tune furnace as follows. The powder used as the carbon-coating agent was glucose (C₆H₁₂O₆, Oriental Chemical Industries, extra pure). The reaction for carbon coating on the particles prepared by chemical reduction is given by

When C₆H₁₂O₆ is decomposed, the decrease in weight is 60%, and 40% remains as carbon. The weight of the glucose was determined by planning the Co-based powder containing 20 wt% coated carbon after C₆H₁₂O₆ decomposed to carbon on the Co-based powder. The mixed weight ratio of the Co-based powder to the C₆H₁₂O₆ powder was 61.54 : 38.46. A determined weight of the C₆H₁₂O₆ powder was dissolved in distilled water with a spoon until precipitates were not observed and then mixed with the dried Co powder. The particles were then dispersed by an ultrasonic cleaner and dried. This dried powder was heat-treated at 700°C for 1 h in Ar atmosphere.

The BET surface areas of the synthesized powders were measured by a BET surface characterizing analyzer (ASAP2010 and TriStar 3000 (Micromeritics, USA)).

The microstructures of the prepared samples were observed by FE-SEM (field emission scanning electron microscope, JXA-8600).

Co-based powder anodes were fabricated by dispersing the powders, carbon (10 wt% or 20 wt%), and polyvinylidene fluoride (PVDF) binder (10 wt%) in N-methyl-2-pyrrolidone (NMP) to form a slurry, which was spread onto copper foil. After drying the coated slurry at 80°C for 12 h in vacuum, the copper foil coated with the slurry was rolled under a pressure of 100 kgf/cm². The coated electrode was punched with a Φ14.6 mm punch. Li/Co-based powder coin cells (type 2016) were then assembled. Li foil metal was used as the counter and reference electrodes. The electrolyte was 1 M LiPF₆ in a 1 : 1 (volume ratio) mixture of ethylene carbonate (EC) and diethyl carbonate (DEC). The charge-discharge tests and CV (cyclic voltammetry) tests were performed with a charge-discharge tester (WBCS3000, WonATech Ltd.). The cells were charged and discharged at a current density of 0.2 mA/cm² in a voltage range of 0.001 V–2.5 V versus Li/Li⁺.

3. Results and Discussion

The XRD patterns of the Co-based powders prepared by chemical reduction method with and without CTAB are shown in Figure 2. The prepared powders are amorphous without crystalline peaks in their X-ray diffraction patterns.

Figure 3 presents the FE-SEM (field emission scanning electron microscope) micrographs of Co-based powders prepared by chemical reduction method, (a)–(c) with CTAB and (d)–(f) without CTAB. The particles were dispersed by an ultrasonic cleaner and dried to observe the microstructure by FE-SEM. The effect of the decrease in grain size can be obtained by the chemical reduction method, since the solute in the solution instantly reacts with the reducing agent. This can be seen clearly in Figure 3. The grain size in the sample prepared with CTAB has a wide particle size distribution between about 100 nm and 10–20 nm. The grain size in the sample prepared without CTAB is quite homogeneous with a grain size of about 20 nm. In the sample prepared without CTAB, the fine grains are agglomerated, which can be seen distinctly in the micrographs at high magnifications.

(a)

(b)

(c)

(d)

(e)

(f)

The TGA-DTA results of Co-based powders prepared by chemical reduction method (a) with CTAB and (b) without CTAB are shown in Figure 4. Just after the chemical reduction and drying, the Co-based powders were used for these measurements, in which the temperature was increased to 1,000°C at a heating rate of 10°C/min in an Ar atmosphere. The absorption peak at 139.86°C in Figure 4(a) does not appear in Figure 4(b). This absorption peak is believed to result from the decomposition of CTAB. The weight decreases rapidly at the beginning (<200°C) in Figures 4(a) and 4(b). This is believed to be due to the evaporation of the distilled water, ethanol, and water vapor adsorbed during storage. The distilled water and ethanol are those which had not been removed during the chemical reduction. The crystallization of Co is expected to occur at about 656.78–730.50°C. This can be verified in the XRD results obtained after heat treatment at 700°C.

(a)

(b)

Figure 5 shows the XRD patterns of Co-based powders prepared by chemical reduction with and without CTAB and carbon-coating heat treatment at 700°C for 1 h. Clear peaks corresponding to Co grains appear. Using the Scherrer formula for the main Co peaks, the grain size of the particles prepared with CTAB and carbon-coated was calculated as 33 nm, which was larger than that of 25 nm obtained for the particles prepared without CTAB and carbon-coated. The XRD patterns of Co-based powders prepared by chemical reduction with and without CTAB and carbon-coating heat treatment at 500°C showed that these Co-based powders were not crystallized, as they were just after chemical reduction.

According to Saida et al. [29], the reaction mechanism of Co powder by chemical reduction is as follows:

These reactions equations show that the reaction between and Co produces Co or Co₂B. The formation of Co in this work suggests that reaction (2) occurs, forming and H₂O.

The FE-SEM micrographs of Co-based powders prepared by chemical reduction (a, b) with CTAB and (c, d) without CTAB and carbon-coating heat treatment at 700°C for 1 h are shown in Figure 6. The particles prepared with CTAB and carbon-coated are larger than those prepared without CTAB and carbon-coated. The particles are believed to have increased in size due to the formation of carbon-coated layers. The particles prepared without CTAB and carbon-coated are spherical, while those prepared with CTAB and carbon-coated have square shapes with edges.

(a)

(b)

(c)

(d)

CTAB was added because we expected its addition to facilitate pore formation. The Co-based powder prepared by chemical reduction without CTAB and carbon-coating heat treatment at 500°C for 1 h had a BET surface area of 3.80 m²/g, indicating a high specific area of the powder. The size of these Co-based particles was calculated as 180 nm from the equation, particle size = 6/(specific surface area × density), by assuming the particles are spherical. The BET surface area of the Co-based powder prepared by chemical reduction with CTAB and carbon-coating heat treatment at 500°C for 1 h could not be measured due to the difficulty in the maintenance of vacuum. So, it was hard to verify that the addition of CTAB facilitates pore formation.

Figure 7 shows the discharge capacity versus cycle number of Co-based electrodes prepared by chemical reduction with and without CTAB and carbon-coating heat treatment at 700°C for 1 h. The Co-based powder prepared with CTAB and carbon-coated has a smaller first discharge capacity (about 557 mAh/g) than the Co-based powder prepared without CTAB and carbon-coated (about 628 mAh/g). A decrease in particle size of the host material is believed to be able to buffer the volume expansion involved during charge and discharge. Even though the volume expansion was minimized by preparing nanosized particles, at the beginning of cycling, the discharge capacity decreases quite abruptly. This is believed to be due to the formation of an SEI (solid electrolyte interphase), which obstructs the movements of Li ions and electrons. However, from the third cycle, the two samples exhibit quite good cycling performances, and the Co-based powder prepared with CTAB and carbon-coated has a better cycling performance than the Co-based powder prepared without CTAB and carbon-coated. The reason why these two samples exhibit quite good cycling performance from the third cycle is believed to be due to the carbon-coated layer which prevents the formation of SEI (solid electrolyte interphase) layers between anode materials and electrolyte.

Poizot et al. [30] reported that electrodes made of nanoparticles of transition-metal oxides (MO, where M is Co, Ni, Cu, or Fe) demonstrated electrochemical capacities of 700 mAh/g, with 100% capacity retention for up to 100 cycles and high recharging rates. Carbon-coated silicon anodes were reported by Dimov et al. [31] to have a charge capacity of 1,080 mAh/g at the first cycle and a charge capacity of 1,270 mAh/g at the second cycle, at the current density of 1 mA/cm². Yue et al. [21] reported that the C/Co electrode, in which Co nanoparticles are embedded in carbon matrix, had a reversible capacity of over 600 mAh/g at a current of 50 mAh/g after 40 cycles. Kim et al. [17] reported that the Li/Co cell, fabricated with the nanosized Co powder synthesized by a pulsed wire evaporation method, had a capacity of 440 mAh/g at the first discharge and a reversible capacity of about 280 mAh/g after 30 cycles. The Li/carbon-coated graphite electrodes were reported by Lee et al. [32] to have a reversible capacity of approximately 350 mAh/g. The Li/Co-based cells of this work have smaller discharge capacities than those of nanoparticles of transition-metal oxides [30] and carbon-coated silicon anodes [31] and have the discharge capacities similar to those of the C/Co electrode, in which Co nanoparticles are embedded in carbon matrix [21]. However, the Li/Co-based cells of this work have larger discharge capacities than those of the Li/Co cell fabricated with the nanosized Co powder synthesized by a pulsed wire evaporation method [17] and the Li/carbon-coated graphite electrodes [32].

The curves of voltage versus time at the first cycle of the Co-based electrodes prepared by chemical reduction with and without CTAB and carbon-coating heat treatment at 700°C for 1 h are shown in Figure 8. The two Co-based electrodes have very similar plateau voltages of about 1 V, and the plateau voltage of the Co-based electrode prepared with CTAB and carbon-coated decreases earlier. These plateau voltages are very similar to that (0.7 V) of the Li/Co cell fabricated with the nanosized Co powder prepared via a pulsed wire evaporation method by Kim et al. [17].

4. Conclusions

Nanosized amorphous Co-based powders could be synthesized by a chemical reduction method in which a reducing agent is added to Co ions dissolved in an aqueous solution. When the prepared nanosized Co powders were subjected to carbon-coating heating treatment at 700°C for 1 h, the amorphous phase was crystallized, and a Co single phase could be obtained. The grain size of the particles prepared by chemical reduction with CTAB and carbon-coating heat treatment was calculated as 33 nm, which was larger than that of 25 nm obtained for the particles prepared by chemical reduction without CTAB and carbon-coating heat treatment. The Co-based powder prepared with CTAB and carbon-coated had a smaller first discharge capacity (about 557 mAh/g) than the Co-based powder prepared without CTAB and carbon-coated (about 628 mAh/g). However, from the third cycle, the former had a better cycling performance than the latter. Even though the volume expansion was minimized by preparing nanosized particles, quite an abrupt decrease in the discharge capacity observed at the beginning of cycling is believed due to the formation of an SEI, which obstructs the movements of Li ions and electrons. The carbon-coated layers are believed to have led to quite good cycling performances of the prepared Co-based powders from the third cycle.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgment

This research was performed for the Research Program funded by Korea Institute of Materials Science (KIMS) in South Korea.

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Copyright © 2014 Seong-Hyeon Hong 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.

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