Xiangyun Zengab,
Liuxue Shiab,
Linjie Liab,
Jiao Yangab,
Xi Chengab and
Meizhen Gao*ab
aKey Laboratory for Magnetism and Magnetic Materials of Ministry of Education, Lanzhou University, 730000 Lanzhou, People's Republic of China
bSchool of Physical Science and Technology, Lanzhou University, Lanzhou, Gansu 730000, People's Republic of China. E-mail: zengxy08@163.com; gaomz@lzu.edu.cn; Tel: +86 931 8914160
First published on 31st July 2015
In this paper, hierarchical ZnMn2O4 microspheres assembled with porous nanosheets have been synthesized by a facile solvothermal process and post annealing method. A possible formation mechanism for this unique structure is proposed based on a detailed time-dependent investigation. As a virtue of its beneficial structural features, the electrochemical tests of the as-synthesized hierarchical ZnMn2O4 microspheres exhibit an enhanced lithium storage capacity and an excellent cycling stability (662 mA h g−1 at 100 mA g−1 after 120 cycles). This may be attributed to their unique structural features of favoring the diffusion of Li+ ions and electrode–electrolyte contacts during the electrochemical reaction and enhanced structural integrity with sufficient void space for buffering the volume variation during the Li+ insertion and extraction. These results indicate that hierarchical ZnMn2O4 microspheres assembled with porous nanosheets are promising anode materials for highly reversible lithium-ion batteries.
Among various binary metal oxides above, Mn based anodes are considered as very promising electrode materials, because manganese is more environmentally benign, much cheaper and more abundant in nature compared to cobalt. Apparently, these prominent features make Mn based binary metal oxides ideal materials to replace Co3O4 as electrode materials. ZnMn2O4 is selected as the research material because of its excellent chemical and physical properties, such as its high theoretical capacity of 784 mA h g−1.10 Recently, some research results on ZnMn2O4 with different nanostructures as high-capacity anodes for lithium-ion batteries have been reported. For example, Zhang et al. have synthesized ZnMn2O4 superstructures with capacity values as high as 626 mA h g−1 after 50 discharge–charge cycles at a current rate of 100 mA g−1.27 Lou and co-workers have described a facile method to prepare ZnMn2O4 hollow microspheres exhibiting a high discharge capacity of 607 mA h g−1 after 100 discharge–charge cycles at 400 mA g−1.10 Recent reports showed that orientated self-assembled/self-supported microsphere structures can help to enhance electrochemical performance because they can enhance the electrochemical kinetics, shorten the diffusion distance for lithium ions and accommodate the volume change during the lithium intercalation and de-intercalation processes.13,28–32
Herein, we present a facile solvothermal method to directly synthesis the hierarchical flowerlike ZnMn2O4 precursor microspheres, which assembled with nanosheets. The formation mechanism of the flowerlike hierarchical microspheres structure has been studied. After an annealing treatment at high temperature under 600 °C in air, highly crystalline hierarchical ZnMn2O4 microspheres assembled with porous nanosheets can be obtained. In addition, we demonstrate that such hierarchically structured spinel ZnMn2O4 porous nanosheets-based microspheres exhibit superior rate capability and cycling stability as cathode materials for LIBs.
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Fig. 1 (a and b) SEM images of the precursor of flowerlike ZnMn2O4 microspheres, (c) XRD pattern, (d) FTIR spectrum and (e) TGA of the precursor of flowerlike ZnMn2O4 microspheres. |
In order to obtain a better understanding of the formation mechanism of the flower-like ZnMn2O4 hierarchical superstructures, the products formed at different growth stages are collected and examined by SEM. The morphologies are shown in Fig. 2. In the initial stage, the precursors are microspheres composed with nanoparticles and some small nanosheets on the surface (Fig. 2a and b). After 3 h of hydrothermal treatment, both microspheres and the hierarchical structures can be found, but the nanosheets are loose and irregular (Fig. 2c and d). After 6 h, the superstructures then gradually ripe, however there are still a few spheres as shown in Fig. 2e and f, and the compact density of the nanosheets is not high. Finally, the perfect flower-like ZnMn2O4 hierarchical microspheres assembled with highly compact porous nanosheets are obtained after 12 h (Fig. 2g and h).
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Fig. 2 SEM images of the precursor of flowerlike ZnMn2O4 microspheres prepared with different reaction durations. (a and b) 1.5 h; (c and d) 3 h; (e and f) 6 h; (g and h) 12 h. |
Based on the time-dependent experiment results, the formation mechanism of the flower-like ZnMn2O4 hierarchical microspheres is proposed to proceed via a four-step process as depicted in Fig. 3. The first step consists of precipitation of metal alkoxide particles from ethanediol solutions of salts. A number of nuclei generate during the initial period and subsequently form primary particles by diffusion of metal glycolates or alkoxide molecularly to the nuclei. (Step I) During the solvothermal process, the main metal glycolates or alkoxide molecular resulting from acid–base equilibrium reactions are believed to form as follows:36,37
HOCH2CH2OH ↔ CH3CHO + H2O | (1) |
CH3COO + H2O ↔ CH3COOH + OH− | (2) |
HOCH2CH2OH + 2OH− ↔ (CH2)2(O−)2 + H2O | (3) |
(CH2)2(O−)2 + Zn2+ ↔ (CH2)2(O)2Zn | (4) |
(CH2)2(O−)2 + Mn2+ ↔ (CH2)2(O)2Mn | (5) |
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Fig. 3 Illustration of the formation of ZnMn2O4 hollow flowers through the Ostwald ripening process. |
In the following stage, these primary particles quickly aggregate into nanospheres driven by the minimization of surface free energy with a size on the micrometer scale, which serve as the cores of the flower-like structures. This particular aggregation process of the particle formation of various monodispersed oxides has been reported by Ocana et al.38 and the formation of microspheres seems to follow the scheme proposed by LaMer et al.39 Moreover, the surfactant molecules providing coordination sites for cations can cap on the surface of the nanospheres, which may be helpful for avoiding the over growth of the nanospheres, resulting in uniformly discrete products, and the EG can act not only as a solvent in the process, but also as a stabilizer to prevent the particles from agglomerating.31,40 (Step II) Meanwhile, the concentration of the reactants in the surrounding solution decreases, which bring about the fall of the supersaturation and a chemical equilibrium is established between the solid–liquid interface. As the hydrothermal reaction proceeds, some interior crystallites are still in nonequilibrium state. In this process, the exterior crystallites will serve as starting points to attract the interior metastable crystallites underneath the surface layer.41 In order to recover the solution from the nonequilibrium state, many of the nanocrystallites in the solution transfer onto the nanospheres, which results in secondary deposition on the exterior surface.12 Owing to highly intrinsic platelike growth habit of zinc oxides and manganese oxides and a simple array of the nanoplates will easily generate a curvature, the new deposition process results in surface nanoflakes.23,42 (Step III) At the last stage, some nanoplates continue to grow larger by combining with remaining particles in the solution with increasing aging time, the inner core is consumed through this dissolution–recrystallization process, possibly because of Ostwald ripening according to the well-known Gibbs–Thomson law.43 The beautiful flower-like ZnMn2O4 hierarchical microspheres consisting of nanosheets are obtained when the inner core is completely consumed. (Step IV).
Fig. 4 shows the general and high-magnification SEM images of the final product, which obtained after treating the as-prepared precursor at 600 °C for 5 h in air. The low-magnification SEM image (Fig. 4a) reveals that the as-made ZnMn2O4 products are uniform and monodisperse microspheres with diameters of 4–6 μm without structural collapse. Compared with the as-prepared precursor (Fig. 1a), after thermal decomposition at 600 °C for 5 h, the ZnMn2O4 products still maintain the structure and morphology integrity and the hierarchical microstructures are quite thermally stable. The high-magnification SEM images (Fig. 4b and c) further indicate that these microspheres assembled with nanosheets, which have the thickness of 50–80 nm. The EDS spectrum (Fig. 4d) reveals that these nanostructures are mainly composed of the elements Zn, Mn and O and the Mn/Zn ratio perfectly agrees with that in ZnMn2O4, indicating that pure flowerlike ZnMn2O4 microspheres are obtained. The silicon peak is considered to be caused by the silicon substrate.
The XRD pattern of the product is shown in Fig. 5a. All of the diffraction peaks in this pattern could be assigned to tetragonal ZnMn2O4 structure, which are in a good agreement with the standard values (JCPDS: 24-1133). No peaks of impurities can be detected from this pattern. The detailed structure of hierarchical ZnMn2O4 microspheres is further characterized by transmission electron microscope (TEM) as shown in Fig. 5b. In agreement with the above described FESEM observation, the TEM image of a single hierarchical ZnMn2O4 microspheres clearly demonstrate that the microspheres assembled with porous nanosheets, which have the thicknesses of 50–80 nm. Fig. 5c shows the HRTEM image of microspheres, from which the interlayer distance of randomly selected nanosheet is calculated to be 0.25 nm, which corresponds well to the lattice spacing of the (211) plane of tetragonal ZnMn2O4.
XPS was used to further confirm the formation of ZnMn2O4. As shown in Fig. 6a, the signals of Zn, Mn and O as well as C can be identified. The presence of carbon at 284.8 eV in the spectrum can be assigned to carbon contamination. The Mn 2p spectrum displays a 2p3/2 and 2p1/2 spin–orbit doublet at 642.5 and 653.9 eV as presented in Fig. 6b. The separation of the two signals is 11.4 eV, which is consistent with the MnIII in ZnMn2O4 materials reported previously,44 and strongly confirms the fact that the MnIV has been completely reduced. Fig. 6c shows the Zn 2p peaks at binding energies of 1021.6 and 1044.5 eV, which can be attributed to the Zn 2p1/2 and Zn 2p3/2 respectively. Additionally, the energy difference between the Zn 2p1/2 and Zn 2p3/2 peaks is 22.9 eV, which is in line with previous reports.45 Meanwhile, O 1s spectra of ZnMn2O4 can be found at 529.9 eV, which is a characteristic of oxygen in metal oxides (Fig. 6d).46
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Fig. 6 XPS spectra of the ZnMn2O4 samples: (a) survey spectrum; (b) Mn 2p spectrum; (c) Zn 2p spectrum; (d) O 1s spectrum. |
Fig. 7 shows the nitrogen adsorption–desorption isotherms and the corresponding Barrett–Joyner–Halenda (BJH) pore size distribution curves of the obtained flower-like ZnMn2O4 microspheres. The adsorption isotherm for flower-like ZnMn2O4 microspheres is a typical IV curve, indicating mesoporous characteristic. The measured Brunauer–Emmett–Teller (BET) area is 26.1 m2 g−1, and the average pore diameter of ZnMn2O4 is about 20.1 nm, which is calculated from the desorption branch of the nitrogen isotherm with the BJH method. The corresponding BJH desorption cumulative pore volume is about 0.1309 cm3 g−1. In consideration of the mesoporous structure of ZnMn2O4 microspheres, it's expected to improve the electrochemical performance by favoring the diffusion of Li+ ions and electrode–electrolyte contacts during the electrochemical reaction.
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Fig. 7 Nitrogen adsorption–desorption isotherm of the ZnMn2O4 microspheres, the inset shows the pore size distribution. |
In order to examine the potential application of the flowerlike ZnMn2O4 microspheres as anode for lithium-ion batteries, lithium storage properties of the obtained materials are tested using the standard ZnMn2O4/Li half-cell configuration at room temperature (RT = 25 °C). Fig. 8a shows typical charge–discharge curves for the first and second cycles of the ZnMn2O4 electrode at a current density of 100 mA g−1 in the potential range between 0.01 and 3.00 V. During the first discharge, the voltage decreased steeply to approximately 1.4 V, whereupon a small plateau sets with 0.15 mol of lithium ion intercalation reaction, a large and steady plateau at 0.5 V with overall capacity of ∼870 mA h g−1 (corresponds to ∼7.8 mol of Li per mol of ZnMn2O4) follows by a slope till 0.005 V and a capacity of ∼359 mA h g−1 (∼3.8 mol of Li). The overall first discharge capacity 1259 mA h g−1 corresponds to ∼11.6 mol of Li, which is higher than the theoretical value (1008 mA h g−1) based on the reaction: ZnMn2O4 + 9Li + 9e− → ZnLi + 2Mn + 4Li2O. The extra Li consumption could be attributed to the decomposition of the electrolyte at low voltages generating a solid electrolyte interphase (SEI) layer and a polymeric gel-type layer at the ZnMn2O4/electrolyte interface. The first charge curve from 0.01 to 3.00 V shows a steady and smooth voltage increase with an overall specific capacity of 707 mA h g−1, indicating a different electrochemical mechanism from the first discharge. Thus, there is an irreversible specific capacity loss between the first discharge and charge cycles. The large irreversible capacity loss of the first cycle might be caused by the phenomenon that the formed SEI film could not decompose completely during the first charge. The voltage–capacity profile of ZnMn2O4 for the second discharge reaction is at variance with the first-discharge reaction (Fig. 7a). The potential plateau shifts upward to nearly 0.60 V (versus Li+/Li) with a more sloping profile accompanied by the disappearance of the small plateau at about 1.40 V. Nevertheless, the overall discharge capacity of 750 mA h g−1 in the second discharge process is retained. The initial charge capacity and the second discharge capacity are 707 and 750 mA h g−1, that match well with the theoretical value (784 mA h g−1) based on the reaction: ZnLi + 2Mn + 3Li2O ↔ ZnO + 2MnO + 7Li+ + 7e−.
Fig. 8b shows the discharge and charge capacity versus cycle numbers up to 120 cycles. As can be seen, the charge capacity decreases gradually to 388 mA h g−1 for the first 70 cycles. Interestingly, the capacity then starts to increase and a high discharge capacity of 662 mA h g−1 is retained after 120 discharge–charge cycles, corresponding to 88% of the second discharge capacity, demonstrating the high reversible specific capacity and long cycle life of the anode. It is interesting to note the phenomenon of the gradual increased capacity, which is well-documented in the literature, and is attributed to the reversible growth of a polymeric gel-like film resulting from kinetically activated electrolyte degradation.35,47,48 To better understand the electrochemical behavior of the flowerlike ZnMn2O4 microspheres, the rate performance at various current densities (50–800 mA g−1) in the voltage range of 0.01–3.0 V is also investigated and shown in Fig. 8c. The cell shows good rate capability with average discharge capacity of 557, 460, 375, 276, and 201 mA h g−1, when the current density increases stepwise to 50, 100, 200, 400, 800 mA g−1, respectively. After high-rate charge–discharge cycling, the current density is reduced stepwise to 50 mA g−1, with a specific capacity as high as 477 mA h g−1 recovered. The improved electrochemical performance of ZnMn2O4 might be partly attributed to its unique structure of assemblies of nanoplates. On one hand, the micro-sized hierarchical structure composed of nano-sized nanoplates with pores effectively increases the electrode–electrolyte contact area for more Li+ migration across the interface, shortens the Li+ ion and electrons diffusion length, and accommodates the structural strain and volume change during the charge and discharge cycle, thus leads to high specific capacity and superior rate capability. On the other hand, the open space between neighboring nanoplates allows for easy diffusion of the electrolyte, ensuring every nanoplate can take part in the electrochemical reaction because each nanoplate is in contact with electrolyte.
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