CC BY
0Hindawi Publishing Corporation
Journal of Nanomaterials
Volume 2012, Article ID 905157, 19 pages
doi:10.1155/2012/905157
Review Article
3D Self-Supported Nanoarchitectured Arrays Electrodes for Lithium-Ion Batteries
Xin Chen,1 Ying Du,1,2 Nai Qing Zhang,2,3 and Ke Ning Sun2,3
1 Department of Chemistry, Harbin Institute of Technology, Harbin, Heilongjang 150001, China
2 Academy of Fundamental and Interdisciplinary Sciences, Harbin Institute of Technology, Harbin, Heilongjang 150001, China
3 State Key Laboratory of Urban Water Resource and Environment, Harbin Institute of Technology, Harbin, Heilongjang 150001, China
Correspondence should be addressed to Ke Ning Sun, keningsun@yahoo.com.cn
Received 17 October 2012; Accepted 3 December 2012
Academic Editor: Jianmin Ma
Copyright © 2012 Xin Chen 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.
Three-dimensional self-supported nanoarchitectured arrays electrodes (3DSNAEs) consisting of a direct growth of nanoarchitectured arrays on the conductive current collector, including homogeneous and heterogeneous nanoarchitectured arrays structures, have been currently studied as the most promising electrodes owing to their synergies resulting from the multistructure hybrid and integrating heterocomponents to address the requirements (high energy and power density) of superperformance lithium ion batteries (LIBs) applied in portable electronic consumer devices, electric vehicles, large-scale electricity storage, and so on. In the paper, recent advances in the strategies for the fabrication, selection of the different current collector substrates, and structural configuration of 3DSNAEs with different cathode and anode materials are investigated in detail. The intrinsic relationship of the unique structural characters, the conductive substrates, and electrochemical kinetic properties of 3DSNAEs is minutely analyzed. Finally, the future design trends and directions of 3DSNAEs are highlighted, which may open a new avenue of developing ideal multifunctional 3DSNAEs for further advanced LIBs.
1. Introduction
Currently, extensive concern about the increasingly worsened environmental pollution and impending exhaustion of limited energy resources has brought about the ever-going demand for seeking renewable and clean energy sources to cope with these serious energy and environmental issues [ 13]. As a suitable energy source, lithium ion batteries (LIBs) are being exploited for the widespread applications [4-7] in portable electronic consumer devices, electric vehicles, and large-scale electricity storage in intelligent grids, due to the multiple superiorities such as high energy density, safety, long life, low cost, and environmental benignity.
A typical commercial LIB consists of a positive electrode (cathode) formed from layered LiCoO2, a nonaqueous liquid electrolyte, and a graphite negative electrode (anode) in Figure 1(a). During the charging process, lithium ion (Li+) is deintercalated from the layered LiCoO2 host, passes through the electrolyte, and is intercalated between the graphite
layers. Vice versa, discharge reverses this process. The electrons, of course, pass across the external circuit [8]. To realize the charge and discharge, the commercial LIBs are commonly constructed by electrodes and the electrolyte trapped within a polypropylene separator, in which electrodes are fabricated by the slurry procedure involved in mixing active electrodes materials with conducting carbon and polymeric binders and then casting them onto the current collector in Figure 1(b).
The electrodes materials are rated on the basis of their specific (gravimetric) capacity (mAhg-1), determined by their charge/discharge graphs, and the degree of capacity change upon cycling at different demands. Intense scrutinized cathode materials, mainly including LiCoO2, LiMn2O4, LiNi^MnyCozO2, LiFePO4, and V2O5 [9-13], have their own unique structured merits, offering highly accessible Li+ diffusion pathways and demerits like limited specific capacities as well as poor capacity retention [14, 15]. Anode materials, such as carbon, silicon, alloy, metal oxides,
Cathode materials
Separator Anode materials
Active materials
Carbon
LiCoO2
Electrolyte
Graphite
3D self-supported nanoarchitectured arrays electrodes (3DSNAEs)
Figure 1: Schematic showing (a) operating principles and components of the typical commercial cylindrical lithium ion batteries (LIBs), (b) the slurry procedure of fabricating commercial electrodes, and (c) the configuration of novel 3D self-supported nanoarchitectured arrays electrodes (3DSNAEs).
and metal sulfides/phosphides, exhibit high capacities and couple to the poorly structured stability and volume variation issues [16-24]. No matter how creative researchers design new lithium intercalation materials, one drawback exists due to the intrinsic diffusivity of Li+ in the solid state (ca. 10~8cm2s_1), which unavoidably limits the charge/discharge performance [25]. In this regard, many efforts have been devoted to devise a variety of nanomaterials with unique structures from zero-dimensional nanoparticles and one-dimensional (1D) nanowires to three-dimensional (3D) micro-/nanostructures and hollow- and core-shell structures, resulting in improved electrochemical performance to satisfy the demands of industrial applications [25-31].
These nanomaterials aforementioned have great superiorities [1, 32, 33] over their bulk counterparts. The reduced dimensions of materials shorten the Li+ and electron transport length, leading to higher capacity at high rates. Meanwhile, a high surface area allows a large contact interface between the electrode material and electrolyte and enhances the Li+ flux across the interface, resulting in a higher capacity. In addition, the small size could accommodate the strain associated with intercalation, reducing the capacity losses. However, nanomaterials are not a panacea to a certain extent and have some disadvantages [34, 35]
such as more side reactions with the electrolyte due to the high electrolyte/electrode surface area, weak structure stabilities induced by aggregations, and lower volumetric energy density compared with microscale materials.
To transcend the above limitations of nanomaterials, selecting a proper approach, a proper structure, and a proper combination of various materials to assemble the active materials into the desired structures is indispensable. Recently, a novel configuration of 3D self-supported nanoarchitectured arrays electrodes (3DSNAEs) in Figure 1(c) has attracted much attention owing to the combination of diversified nanostructures' merits, including high surface in favor of high capacity, ordered and stable structures to the benefit ofbuffering for the volume change and improving the electric conductivity of electrodes, and lower aggregation and collapse in comparison to nanoparticles [36-38]. This kind of 3DSNAEs consists of a direct growth of nanoarchitectured arrays on the conductive current collector, providing a direct pathway for efficient charge transport along the arrays axis and forming a 3D conductive network among active materials, nanoarchitectured arrays pathways, and the conductive current collector. Differencing from the traditional slurry procedure, each nanoarchitectured array of 3DSNAEs is directly connected to the current-carrying substrate without any conductive and binder agents and allows for all
structures' contribution to the capacity and efficient charge transport, leading to the excellent electrochemical properties [37,39, 40].
In this paper, detailed investigations are focused on strategies for the fabrication, selection of the different current collector substrates, and structural configuration of 3DSNAEs with different cathode and anode materials for LIBs. The intrinsic relationship of the unique structural characters, the conductive substrates, and electrochemical kinetic properties of 3DSNAEs is minutely analyzed, and recent work by our group is also summarized. Finally, the problems and prospects are highlighted on this kind of 3DSNAEs.
2. Strategies for Fabrication
Nanoarchitectured arrays of 3DSNAEs, including 1D nanowires (NWs), and nanotubes (NTs), nanorods (NRs), are apparently influenced by their properties of the conductive substrates, owing to the unique structures that nanoarchitectured arrays are directly grown on the current collector substrates. Different strategies, therefore, should be made to fabricate the 3DSNAEs grown on the different substrates. To the best of our knowledge, the conductive substrates applied in the 3DSNAEs principally contain Al, Cu, Ti, Ni, Au, Si, stainless steel (SS), Fe-based alloy, Sn-doped In2O3 (ITO), and so on. And the strategies to fabricate 3DSNAEs may be classified into 3 categories in Figure 2, namely, self-growing, wet-etching, and template-based growth.
Self-growing in Figure 2(a) is the one for fabricating the nanoarchitectured arrays directly grown on the substrates by using a variety of techniques such as vapor phase growth, hydro-/solvothermal growth, and solution-based growth. Vapor phase growth including thermal chemical vapor deposition (CVD), direct thermal evaporation [41], and pulsed-laser deposition (PLD) is a straightforward way that controls the reaction between oxygen gas and metal vapor source in the light of vapor-liquid-solid and vapor-solid mechanisms [42, 43]. CVD involves the process of growing the nanoarchitectured arrays on the substrate surface via the chemical reaction in the gas phase, which is resulted from the vapor with the element ofnanoarchitectured arrays and other indispensable gases in the reactive chamber. By using the CVD approach, Si NWs [37] and V2O5/SnO2 NWs [44] could be directly grown on the SS substrate, and V2O5 nanoribbons [45] would be also done on the Si substrate. Whilst employing the thermal evaporation technique, Si nanopillars [46] and SnO2 NWs [47] could be orderly grown on the SS substrate. Besides, hydro-/solvothermal growth is a common method ofpreparing nanoarchitectured arrays grown on the metal or alloy substrate. The process involves the aqueous mixture of soluble metal salt (metal and/or metal-organic) of the precursor material and the treatment of the mixed solution in an autoclave filled under elevated temperature from 100°C to 300°C and relatively high pressure conditions >1atm. Recently, MoOx NRs on the Cu substrate [48], single-crystal mesoporous Co3O4
nanobelts [49] and a-Fe2O3 NRs [50] were prepared via the hydro-/solvothermal method. These approaches aforementioned, however, ordinarily require high temperature or high pressure. By comparison, the solution-based method based on a liquid-solid growth mechanism has been extensively exploited for preparing the free-standing nanoarchitectured arrays at the low temperature, which could reduce considerably the complexity and cost of fabrication [51, 52]. The process is that a piece of substrate immersed in reaction solutions generates a thin film with nanoarchitectured arrays at a low temperature <100°C for a while. For instance, the homogeneous and dense arrays of ZnO NWs grown on arbitrary substrates were produced by Greene et al. via the liquid-solid growth [53], and Li et al. prepared mesoporous Co3O4 NWs arrays on the Ti substrate by the ammonia-induced solution growth [54].
Self-etching in Figure 2(b) involves a pure chemical or electrochemical reaction process, in which the surface layer of the conductive substrates is corroded and converted immediately to nanoarchitectured arrays by using the reactions between solutions and the etching materials. Lately, some considerable efforts have been devoted to fabricate ordered 1D Si nanostructured arrays via a metal-assisted chemical etching approach [55, 56]. The etching process included the following aspects: (a) the oxidant was preferentially reduced on the surface of the noble metal; (b) the holes resulted from the reduction of the oxidant on the noble metal surface and were injected into the Si that was in contact with the noble metal; (c) the Si was oxidized and dissolved at the Si/metal interface by HF. Different from the Si etching, a solution-based corrosion is also to prepare nanoarchitectured arrays [57]. Immersed in alkaline solutions, the surface layers of Cu foil and Ni grid were corroded into 1D CuO arrays [58, 59] and Ni3S2 NW arrays [60], respectively. In addition, self-organized TiO2 NTs arrays [61, 62] had been prepared via electrochemical anodization of Ti foils by controlling the electrolyte composition as well as the rate at which the resultant oxide was dissolved. To be excited, a novel vapor-phase corrosion strategy had been developed by our group to fabricate CuO hierarchically mesoporous nanosheet-assembled gearlike pillar arrays (HMNGPAs) and mesoporous nanosheet cluster arrays (MNCAs) [63, 64]. This strategy involved the oxidation, complexation, and thermal decomposition processes and was simple, low-cost, and broadly applicable, providing a new avenue for large-scale configuration of nanoarchitectured arrays with unique multifunctional properties.
Template-based growth, just as its name implies, is that the employed materials deposited in the template decorated on the substrate surface via a certain chemical or physical approach are transformed to nanoarchitectured arrays by removing the template membrane, as shown in Figure 2(c). The AAO membrane is the most widely used template, because of its facile preparation and the controllable uniformity pore distribution with lower ohmic drop, validating the homogeneous electrolyte flow. For example, arrays of perpendicular Cu nanopillars on the Cu foil substrate were fabricated by Taberna et al. via cathodic electrodepositing of the electrolyte with Cu2+ ion into the pores of AAO
111 III
Substrate
— ■»»III
Composite
Figure 2: Schematic for the fabrication principle of 3DSNAEs by self-growing (a), self-etching (b), and template-based growth (c).
membrane [65]. Kim et al. [66] prepared vertical arrays of MnO2 NWs on the Si substrate by the following steps: (a) sputtering a thick aluminum layer on silicon chips, (b) anodizing the aluminum layer, (c) anodic electrodepositing of MnO2 NWs in the alumina pores, and (d) removing the AAO layer. Besides, by employing the CVD and AAO templates technique, the vertically aligned core-shell Au/CNT-V2O5 NRs arrays on the Al substrate had been synthesized by Kim et al. shown in Figure 3 [67]. Coupled with the previous irrigation from the top of templates, V2O5-TiO2 NRs arrays were prepared by a capillary-enforced template-based method, filling into the pores of a polycarbonate membrane (PC) from the bottom with VOSO4 and TiOSO4 solutions [68].
3. Selecting Substrate
The current collector substrate, as a main component of 3DSNAEs, plays a significant role in the configuration and electrochemical performance of 3DSNAEs. The substrate could be classified into three major categories shown in Table 1: cathode substrate with high oxidation voltage (Al), anodic substrate with high electrochemical stability in a low voltage window (Cu), and multifunctional substrate, on the basis of functions of 3DSNAEs for LIBs.
3.1. Cathode Substrate. Generally, cathode substrate used to load cathode materials (LiCoO2, LiMn2O4, and LiFePO4) requires high oxidation voltage and high electrochemical stability in a wide voltage window. Al with multiple superiorities, such as high oxidation voltage (5 V versus Li/Li+), good electric conductivity, and low price, could be protected by a thin and dense Al2O3 layer. However, in a low voltage close to 0 V (versus Li/Li+), an Li-Al alloying process would happen because of the deposition of dissolved Al3+ from the Al2O3 layer of the Al foil [114, 115]. Therefore, Al is mainly used as the current collector of cathode materials for LIBs. The single-crystal V2O5 NRs and NTs arrays directly connected to the planar Al substrate were fabricated by
Wang et al. via template-based electrodeposition and delivered 5 and 1.3 times higher capacity than sol-gel-derived films at the same current density, respectively [69, 116, 117]. Despite the improved electrochemical performance of V2O5 nanoarchitectured arrays, the planar Al substrate has limited surface area to provide the limited contact between active materials and substrate. In this regard, Ni NRs arrays were firstly grown on the planar Al substrate and then coated with V2O5 to synthesize Ni-V2O5-nH2O nanocable arrays, which delivered approximately 10 times higher capacities single-crystal V2O5 NRs and 20 times higher than sol-gel-derived V2O5 films, due to the large surface and short diffusion path offered by the Ni-V2O5-nH2O nanocable arrays [118]. Afterwards, Al NRs arrays directly grown on the Al foil to construct 3D current collectors for LIBs offered high surface area and facilitated the contribution to the capacity of active materials [119, 120]. For example, a vertically aligned Au/CNT-V2O5 core-shell NRs electrode developed by Kim et al. demonstrated high capacity (473.7 mAh at 1C rate) and excellent rate performance (379.2 mAh at 10C rate) owing to the aligned nanostructures with increased reaction sites, facilitated charge transport, and improved mechanical stability [67].
3.2. Anode Substrate. Cu foil has been extensively used as the current collector of anode materials, because metal Cu with good conductivity hardly forms the Li-Cu alloy at a low voltage and could be oxidized and dissolved at the high voltage (>3.6V versus Li/Li+) [115]. Nickel nanocones arrays (NCAs) which supported Si anode was firstly constructed by Zhang et al. via the electrodepositing and sputtering techniques and delivered a high capacity of 2400 mAh g^1 at 0.2C rate over 100 cycles, because Ni NCAs facilitated charge collection and transport, supported the electrode structure, and acted as inactive confining buffers [121]. Thanks to factors that the chemical property of metal Cu is considerably brisk and easy to be corroded by acid or alkali solutions. The template-based growth is an effective strategy to construct 3DSNAEs on the Cu substrate.
CNT deposition (b) Carbon layer
i) ion milling il) Chemical etching
ï ii M H HR Îï fi ■ » ■■ ai ai » ■* il -i
V2O5 growth = V2O5+
UUiiUIIUIIU
Carbon deposition
Figure 3: Schematic of the fabrication process of Au/CNT-V2O5 core-shell nanorod arrays with the schematized electrochemical reaction involving the nanostructured Li battery electrode [67].
Since Taberna et al. prepared Cu NRs arrays on the Cu substrate to construct Cu NRs arrays supported Fe3O4 via AAO template-based electrodeposition [65], many anode materials such as Cu-Fe3O4 [122, 123], Cu-Sn [74, 124], Cu-Bi [75], Cu-Cu3P [84], and Cu-Ni3Sn4 [18] have been developed by the template-based growth. For example, as the anode materials, Cu-Ni3Sn4 delivered a capacity of 500mAhg_1 with no decay over 200 cycles at 0.8C rate. In addition, solution-based growth is also an efficient way to large-scale fabricateion of 3DSNAEs on the Cu substrate, due to the easy realization of the preparation conditions. By varying these parameters including the ratio of reaction precursor ions, temperature, and immersing time, CuO NTs [58], nanobelts [59], NRs [76], ZnO NRs [77], and Cu2S NWs [83] could be directly grown on the Cu substrate. At 0.5C rate, CuO NRs delivered a high capacity of 650 mAh with no capacity decay even after 100 cycles. Even at a high rate as high as 20C, Cu2S NWs were capable of delivering a reversible capacity of 145 mAh g_1.
Metal Ni is widely available in many forms, such as foil, grid, and felts, and is stable up to 4.5 V (versus Li/Li+), after which the electrodissolution of Ni begins [125]. Ni is commonly used as the current collector of anode materials. Fan et al. reported that freestanding Co3O4 nanosheets on the Ni
foil substrate delivered a reversible capacity of 631 mAh g-1 after 50 cycles at a constant current of 150 mAg-1 in a fixed voltage window from 2.5V to 0.01V [87]. Wu et al. prepared interconnected MnO2 NWs on the Ni foil substrate by electrodeposition, which delivered reversible capacity of 800 mAh g-1 and with low capacity decay after 100 cycles [86]. Additionally, the oriented Ni3S2 NWs arrays on the Ni grid substrate fabricated via the solution-based growth showed a reversible capacity of 430 mAh g-1 with the capacity retention 80% over 100 cycles [60].
Fe is an inexpensive metal and cannot generate Li-Fe alloy at 0 V (versus Li/Li+) during polarization in the cathodic direction; thus, Fe-based alloy substrate could be exploited for loading the metal oxide anode materials to construct 3DSNAEs via the hydro-/solvothermal growth. By controlling the conditions of the hydro-/solvothermal growth, Liu and coworkers have prepared SnO2 NRs [88], C/a-Fe2O3 NTs [89], ZnO/C NRs [90], and SnO2/C NRs [126] directly grown on the Fe-base alloy substrate. The C/a-Fe2O3 NTs retained a reversible capacity of as high as 659 mAh g-1 at 0.2C rate after 150 cycles, and the pristine a-Fe2O3 NTs maintained only 384 mAh g-1 at the same conditions. Such good electrochemical performance may be attributed to the nanoscale intimate contact of a-Fe2O3 with
Table 1: A summary of optimizing various electrode materials and suitable strategies to construct 3DSNAEs on various current collector substrates.
3DSANEs
Collector Materials
Growth method
Remark
Cathode
V2O5 [69], LiCoO2 [70]
-X V2O5-W68U.VO,,,]
CNTs [72], Si [73], metal (Sn, Bi) [74, 75], MO (M = Fe, Cu, Zn, Ni) [65, 76-78], alloy (SnCo [79], NiSn [18, 80, 81], SiGe [82]), Cu2S [83], Cu3P [84], Sn/graphene [85] Ni3S2 [60], MnO2 [86], Co3O4 [87]
Fe-based alloy MO (M = Sn, Fe, Zn) [88-90]
Cathode or anode
The stainless steel
SnO2 [91], CNT-MnO2 [92], SnCo [93]
CNTs [94], Ge [95], Si [37, 96-99], CNT-Si [100], Si/Cu [101], SnO2 [47], lTO/TiO2 [102], Ni/MnO2 [103], Fe2O3/SnO2 [104], V2O5/SnO2 [44], CNTs-LiCoO2 (LiMn2O4) [105], CNTs-LiCoPO4 [106, 107] V2O5 [108], MO (M = Ti, Co, Fe, Sn) [49, 50, 62, 109]
V2O5 [45], Si [56], Si/NiO [110], MnO2 [111], Cu2O [112], Sn [113]
Template-based chemical or physical deposition
Chemical or physical deposition
Template-based chemical or physical deposition
Solution-based growth
Electrodeposition, solution-based growth
Hydrothermal, solution-based growth
Template-based chemical or physical deposition
Needing complicated synthesis techniques
It is a technique for large scale preparation
Needing complicated synthesis techniques
Chemical/physical vapor deposition Needing high
temperature
Anodization, hydro/solvothermal, Solution-based growth Chemical/physical deposition, etching
It is a hope for large scale preparation Needing complicated synthesis techniques
conductive carbon framework and the unique porous tubular nanostructures readily derived from sacrificial template-accelerated hydrolysis.
3.3. Dual Functional Substrate. Dual functional substrate, including SS, Ti, Ni, and Si, could act as cathode or anode substrate, owing to the superiorities such as a high oxidation voltage and non-Li-metal alloying process in a low voltage.
As an inert substrate, SS with a high oxidation voltage (5 V versus Li/Li+) has been widely used as the current collector for LIBs, because the Cr and Fe oxides on the surface protect the metal bulk from general corrosion. To the best of our knowledge, CVD and physical vapor deposition (PVD) are usually developed to construct 3DSNAEs on the SS substrate. Masarapu et al. found that aligned multiwall carbon nanotubes (MWNTs) on the SS substrate obtained by CVD technique delivered an initial capacity of 132 mAh g-1 at 1C rate and a reversible capacity of 460 mAh g-1 after 1200 cycles, attributing to the morphology of the MWNTs with structural and surface defects and the SS substrate' contribution to capacity [94]. Chan and coworkers prepared a series of Si-based nanoarchitectured arrays on the SS substrate by using CVD [37, 72, 95, 97] and found that Si NWs exhibited a stable capacity -3500 mAh g-1 for 20 cycles. Besides, Yan et al. used multistep CVD to construct V2O5/SnO2 NWs with high power density of 60kWkg-1 and energy density of as high as 282Whkg-1 [44]. Such excellent performance might be ascribed to the unique
core/shell structure that the thin V2O5 layer was in favor of the fast Li+ lithiation/delithiation, and the SnO2 core offered a fast path for electron transportation and also increased the utilization of V2O5. By employing PVD technique, the vertical Si nanopillars arrays and single-crystal SnO2 NWs on the SS substrate were also fabricated by Fleischauer et al. [46] and Ko et al. [47]. The SnO2 NWs delivered a high discharge capacity of 510 mAh g-1 after 50 cycles at 1C rate and displayed superior rate capability of 440 mAh g-1 at 10C rate.
Metal Ti is very resistive to the alkaline ammonia solution and oxidation, does not alloy with lithium at low voltage, and therefore is a good current collector material for LIBs [127]. V2O5 nanobelt arrays on the Ti substrate prepared via hydrothermal growth could deliver a reversible capacity of 240 mAh g-1 stably after 50 cycles at the current density of 400 mAg-1, and a high rate capacity of 150 mAh g-1 at 4000 mAg-1 [108]. And the mesoporous Co3O4 NWs arrays on the Ti substrate via solution-based growth exhibited a high reversible capacity of 859 mAh g-1 at the current density of 111 mAg-1 and high rate capacities of 450mAhg-1 at 2220mAg-1 and 240mAhg-1 at 5550mAg-1 [54]. Whilst directly anodizing and annealing Ti foil, the self-organized TiO2 NTs on the Ti substrate could be obtained. Ortiz et al. found that the amorphous TiO2 NTs delivered a highest capacity of 77 ^Ahcm-2, and crystalline TiO2 NTs had the best capacity retention up to 90% over 50 cycles [62]. Wei et al. reported that the TiO2 NTs with 50 nm pore size and 20 nm thickness showed the highest reversible capacity of
180 mAh g-1 over 140 cycles [ 128]. Liu and coworkers found that TiO2 NTs annealed at N2 possessed an initial discharge capacity of 163 mAh g-1 and maintained 145 mAh g-1 over
50 cycles and that TiO2 NTs annealed at CO exhibited an initial capacity of 223 mAh g-1 with the reversible capacity of 179 mAh g-1 at the 50th cycle [129, 130]. The results might be attributed to the presence of surface defects like Ti-C species and Ti3+ groups with oxygen vacancies, improving the charge-transfer conductivity of the arrays and promoting phase transition.
Although Si could form Li-Si alloy at ca. 0.12 V (versus Li/Li+), crystalline Si cores of core-shell crystal-amorphous
51 NWs functioned as not active material store but a stable mechanical support [97]. Therefore, the Si substrate can act as a dual functional substrate for loading cathode or anode materials to construct 3DSNAEs. Chan et al. prepared single-crystal V2O5 nanoribbons via thermal vapor deposition and found that transformation ofV2O5 into the w-Li3V2O5 phase could take place within 10 s in thin nanoribbons, suggesting a significant increase in battery power density [45]. Liu and coworkers found that MnO2^.5H2O nanowall arrays electrodeposited on the Si substrate exhibited a reversible capacity of 220 mAh g-1 over 50 cycles at 0.5C rate and mesoporous MnO2^.5H2O nanowall arrays with 500 nm thickness delivered a stable capacity of 256 mAh g-1 [111, 131]. Such excellent electrochemical performance might be ascribed to the hierarchically structured macro- and meso-porosity of MnO2 ■ 0.5H2O, which offered a large surface area to volume ratio of favoring interface faradic reactions and shortened solid-state diffusion paths. Moreover, Kim et al. prepared vertical arrays of Sn NWs on the Si substrate via AAO template-based electrodeposition [113], which showed the discharge capacity of 400 mAh g-1 after 15 cycles at the current density of 4200 mA g-1.
4. Structural Configuration
As electrodes materials ofLIBs, nanomaterials could enhance charge/discharge kinetics and improve high Li storage capacity, despite of suffering from low thermodynamic stability and surface side-reactions. Optimizing and designing proper nanoarchitectured arrays to take advantages and restrain disadvantages of electrodes materials are, therefore, of particular importance to the electrochemical properties of 3DSNAEs. Types of the 3DSNAEs structure reviewed here contain homogeneous nanoarchitectured arrays and heterogeneous nanoarchitectured arrays (Figure 4).
4.1. Homogenous Nanoarchitectured Arrays. Homogenous nanoarchitectured arrays, namely, single-component nanos-tructure arrays, mainly include simple nanostructure arrays, nanostructure cluster arrays, and nanostructure gearlike arrays on the basis of the structure characteristic of nanoar-chitectured arrays. For this category, nanostructure arrays directly connected to the conductive substrate are used as both the structural support and electroactive materials to alleviate large strain without pulverization and provide good electronic contact and conduction. Electroactive materials
of nanoarchitectured arrays, therefore, are considerably rigorous and should possess the merits including a degree of conductivity and easy growth controll.
Simple nanostructure arrays are commonly composed of single-phase 1D NWs, NTs, and NRs arrays directly connected to the conductive substrate. Up to now, the 1D array materials such as V2O5 nanobelts [108], multiwall carbon nanotubes (MWCNTs) [72, 94], Si NWs [132], Ge NWs [95], Sn NWs [113], SnO2 NRs [88], and MnO2 NWs [86] have been developed to act as the 3DSNAEs with rate capability and cycling stability. V2O5 nanobelts directly grown on a Ti substrate based on the hydrogen bonding action delivered high reversible capacity of 650 and 520 mAh g-1 after 50 cycles at the current density of 1.2 and 3Ag-1, respectively. MWCNTs directly grown on a Cu current collector (MWCNT-on-Cu) in Figure 5 were synthesized by a two-step process of catalyst deposition and CVD and showed a high reversible capacity of 900 mAh g-1 after 50 cycles at 1C rate. Excellent electrochemical properties of MWCNT-on-Cu structure could be ascribed to high Li ion intercalation on the carbon nanotube walls, strongly bonding with the Cu substrate and good conductivity.
Nanostructure cluster arrays, generally, consist of clusters of assembled NWs, NRs, and nanosheets. Because NWs, NRs and nanosheets are usually inclined to aggregate and form the nanostructure clusters due to their structural instability. Some nanostructure cluster arrays, recently, including network-like and flower-like CuO [133, 134], CuO MNCAs [64], and CuO pine-needle-like (PNL) arrays (see Figure 6) [135], have been used as the 3DSNAEs with enhanced lithium storage properties. CuO MNCAs synthesized by our group exhibited a high reversible capacity of 639.8 mAh g-1 after 100 cycles at 1C rate and a high-rate capability of
548.8 mAh g-1 at 10C rate. CuO PNL arrays fabricated by our group via an anodic route delivered high rate capacity of
545.9 and 492.2 mAh g-1 at 15C and 20C rates and exhibited excellent cyclability of 583.1 mAh g-1 after 100 cycles at 2C rate. The enhanced lithium storage properties could be ascribed to the unique nanostructure cluster arrays, which provide suitable branches for lithium storage and suitable free space to facilitate Li+ flux across the interface as well as accommodating the large volume variation.
Nanostructure gearlike arrays. In this respect, the size of arrays directly connect to the substrate is mainly microscale, which is stable and easy to controlled synthesis by a simple approach. Furthermore, microarrays are ordinarily assembled by a mass of nanosheets, NWs, or NBs with the same component, in favor of enlarging the contact areas between active materials and electrolyte. The microscale coglike CuO fabricated by the microemulsion-mediated method exhibited a high reversible capacity of 583 mAh g-1 at a rate of 4C [136]. In our work, CuO HMNGPAs [63] shown in Figure 7 have been synthesized via a novel vapor-phase corrosion strategy and exhibited excellent cycling stability of 651.6 mAh g-1 after 100 cycles at 0.5C rate and high-rate capability of 561.6 mAh g-1 at 10C rate, because the unique HMNGPAs consisting of numerous gearlike pillars assembled by nanosheets could take full advantage of both micro and nano, namely, micropillars with structural
Homogenous nanoarchitectured arrays
Figure 4: Schematic of homogenous nanoarchitectured arrays. (a) Simple nanostructure arrays, (b) nanostructure cluster arrays, and (c) nanostructure gearlike arrays.
Lithiated
De-lithiated CNT
200 [im
1400 1200
Ultralow resistance
High flexibility to accommodate expansion/ contraction
High surface area
Strong bonding with the substrate
ty 1000
rs 400
20 30 40 Number of cycles
Figure 5: (a) SEM images of the as-grown MWCNT-on-Cu structure. (b) Exceptional stability of the reversible capacity of the MWCNT-on-Cu anode in long-run, at 1C rate. (c) A schematic of the proposed lithiation/delithiation mechanism. (d) A schematic of the proposed anode structure [72].
stability and mesoporous nanosheets with high lithium-storage sites.
4.2. Heterogeneous Nanoarchitectured Arrays. Heterogeneous nanoarchitectured array are hybrid nanostructure arrays with multinanocomponents each tailored to satisfy different demands such as high energy density, high conductivity, and excellent mechanical stability. On the basis of the structural characteristic, heterogeneous nanoarchitectured arrays could be classified to six types, including (a) simple heterogeneous nanostructure arrays, (b) coaxial or core/shell heterogeneous
nanostructure arrays, (c) semicoated grenadelike heterogeneous nanostructure arrays, (d) dispersed heterogeneous nanostructure arrays, (e) branched heterogeneous nanos-tructure arrays, and (h) folded heterogeneous nanostructure arrays (Figure 8).
4.2.1. Simple Heterogeneous Nanostructure Arrays. Generally, this kind of structure is composed of 1D array structures with two or more components used as active materials, on the basis of the dual lithium insertion/desertion mechanism. V2O5-TiO2 NRs arrays with molar ratio
N2 Bubble
304 SS
KOH solutions
450 ¡a 450 Ca
10 20 30 40 50 60 Cycle number
Discharge Charge
Figure 6: (a) A schematic of the cell used for the preparation of Cu(OH)2 PNL arrays, wherein CE, WE, and RE represent the counter, working, and reference electrode, respectively. SEM image (b), structural schematic (c), and rate cyclability (d) of CuO PNL arrays gained by annealing Cu(OH)2 PNL arrays [135].
V/Ti = 75/25 prepared by Takahashi et al. could deliver 1.5 times discharge capacity of V2O5 NRs at the current density of 92 mAg"1, resulting from the change of crystallinity and interaction forces between adjacent layers in V2O5 [68]. SnO2/a-Fe2O3 NTs arrays fabricated by Zeng et al. showed high areal capacities of 1.289 mAh cm"2 at a current rate of 0.1 mAcm"2, possibly due to the synergistic lithium storage of SnO2 and a-Fe2O3 electroactive materials [137].
4.2.2. Coaxial or Core/Shell Heterogeneous Nanostructure Arrays. In this case, the coaxial or core/shell structures refer to 1D array inner cores coated completely by other materials as shells. The functions of 1D array inner cores and shells can be both the structural support and electroactive materials on the basis of the particularity of 1D array directly connected to the conductive substrate.
While the 1D array inner cores are only used as the structural support, the outer shells are used as the electroactive materials, and the unique structured materials containing
Al NRs-LiCoO2 (see Figure 9) [70], Cu NRs-Fe3O4 [65], Cu-Si nanocable [138], Cu-Si"Gex NWs [82], hybrid ITO/TiO2 [102], and Ni/Si NWs [139] exhibit a super high-rate performance. For example, the Cu-Si nanocable exhibited a specific capacity as high as 1890 mAhg"1 under a current density of 0.3 A g"1 and 1660 mAhg"1 under a current density of 1.4 A g"1. Hybrid ITO/TiO2 demonstrated an extremely low average capacity fading -0.1% per cycle for 1000 cycles at a current density of 60C. The previous excellent lithium storage properties could be related to the unique Al, Cu, ITO, and Ni 1D nanostructures directly connected to the conductive substrate, which act as inner cores of electroactive materials and form the 3D conductive network of the current collectors, providing both efficient pathways for ion and electron transport, improving the energy density per unit area.
The other strategy is that the 1D array inner cores act as the active materials and the shell as conductive agents (amorphous carbon). The semiconductor metal oxides have been usually constructed to the core/shell Fe2O3/C NTs and
1050 900
— 750
-E 600
■Еу
300 150 0
Discharge Charge
Figure 7: (a) Schematic device of the ammonia vapor-phase corrosion route. SEM images (b), rate cyclability (c), and a schematic diagram of discharge-charge (d) ofCuO HMNGPAs [63].
Heterogeneous nanoarchitectured arrays
Figure 8: Schematic of heterogeneous nanoarchitectured arrays based on structural complexity. (a) Simple heterogeneous nanostructure arrays, (b) coaxial or core/shell heterogeneous nanostructure arrays, (c) semicoated grenadelike heterogeneous nanostructure arrays, (d) dispersed heterogeneous nanostructure arrays, (e) branched heterogeneous nanostructure arrays, and (f) folded heterogeneous nanostructure arrays.
Energy (KeV)
0 20 40 60
Cycle number
■ Charge • Discharge
100 120
Figure 9: SEM images (a), EDX pattern (b), structural schematic (c), and cycling performance (d) of Al NRs-LiCoO2. Insert of (b) shows a TEM image of Al NRs-LiCoO2, and insert of (d) shows an SEM image of Al NRs-LiCoO2 3D electrode cycled 50 times at 0.2C rate [70].
NRs [50, 89], ZnO/C [90], and SnO2/C NRs [126] arrays, wherein metal oxides functioned as both the active core and the structural skeleton, and the carbon shells (nano-Cu) are used to improve the conductivity of materials and suppress the volume expansion. SnO2/C NRs prepared by a two-step hydrothermal method exhibited a high reversible capacity of 585 mAh g-1 after 50 cycles at 500 mAg-1. Furthermore, a new copper-coating layer has better conductivity than carbon and can suppress electrolyte decomposition on the surface of 1D array. Chen et al. found the copper-coated Si NWs showed an initial Coulombic efficiency of 90.3% at a current density of 210 mAg-1 [101].
The third way is that the inner cores and shells are both the active materials to construct the coaxial SnO2 NWs/CNTs [91], hybrid MnO2/CNTs [92], and C-Si NTs sponge [140]. Hybrid MnO2/CNTs delivered the first discharge capacity of 2170 mAh g-1 and a reversible capacity of -500 mAh g-1 after 15 cycles. This kind of material showed the good charge/discharge performance, due to the dual lithium storage mechanism of insertion/desertion, in which CNTs acted as a highly conductive backbone to accommodate the volume expansion and avoid agglomeration.
4.2.3. Semicoated Grenadelike Heterogeneous Nanostructure Arrays. The grenadelike structure is analogous to the core/ shell structure and composed ofinner cores and outer shells. The difference, however, is that the outer shell of grenadelike structures is semicoated. Generally, the inner core is the major component with functional properties, while the outer shell acts as the structural support. Ortiz et al. prepared NWs SnO/NTs TiO2 [141] and NWs Fe2O3/NTs TiO2 (see Figure 10) [142] in the matrix of TiO2 NTs by anodization and electrodeposition. At the current density of 50 ^A cm-2, NWs SnO/NTs TiO2 exhibited a remarkable reversible capacity of about 140 ^Ahcm-2 with the capacity retention of ca. 85% over 50 cycles. The enhanced electrochemical performance could be ascribed to the TiO2 NTs matrix that allows the volume expansion during the Li+ insertion and desertion process.
4.2.4. Dispersed Heterogeneous Nanostructure Arrays. In this dispersed structure, nanomaterials are commonly anchored on the surface of 1D array to be used as the electroactive components or the conductive network for facile electrons transport. While the 1D array (CNTs and Si NWs)
Fe2Û3
700 650 600 550 1= 500 J= 450 400 fr 350 -
« 250 H 1 200 ^ 150 100 50 0
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Number of cycles
20 30 40 Number of cycles
-■— Crystalling ntTiO2
-a— Crystalling ntTiO2 + Fe2O3 microballs
-*— Crystalling ntTiO2 + Fe2O3 nanowires
0.005-3 V
—■— Variable intensity 25 pA cm-2
Figure 10: SEM images (a) and structural schematic (b) of nanocomposite NWs Fe2O3/NTs TiO2, cycling life (c), and rate performance (d) of nanocomposite electrodes [142].
functioned as the electrical conducting pathway and the stable mechanical support for strain release, the anchored nanomaterials including LiCoO2 (LiMn2O4) [105], LiCoPO4 [106, 107], and NiO NWs [110] acted as the electroac-tive components. The binder-free LiCoO2-3wt% SAC-NTs composites could deliver high reversible capacities of 145.7 mAhg-1 at 0.1C rate and 130.4 mAhg-1 at 2C rate. The ordered NiO-coated Si NWs arrays showed a reversible capacity of 606.13 mAh g-1 at the rate of50mAg-1 after 30 cycles. While the dispersed nanomaterials (Ag nanoparticles) are mainly applied to improve the conductive and utilization of the active materials, the Co3O4-Ag NWs arrays exhibited more than 82% capacity retention at the current density of 2000 mAg-1 after 20 cycles, in comparison with 74% capacity retention of the pristine Co3O4 arrays [143]. When 1D array and dispersed nanomaterials are both used as
electroactive materials, these structural materials of VA CNTs-Si [100, 144-146] showed high rate capacities of lithium storage. For instance, VA-CNTs/Si arrays shown in Figure 11 via a two-step CVD technique exhibited high discharge capacities of 2980, 1890, and 765mAhg-1 at 1.3C, 5C and 15C rate, respectively.
4.2.5. Branched Heterogeneous Nanostructure Arrays. Being similar to core-shell structure, branched heterogeneous nanostructure arrays, generally, consist of an inner core and outer shell with a branched structure and possess both all desired functions of each component and a strong synergetic enhancement. More specifically, the inner core provides a direct pathway for electron transport, while the outer shell maintains the structural stability of the inner core during the discharge-charge process. The core-shell Ni/MnO2 hybrid
0 50 100
Cycle number
Figure 11: SEM (a, b), TEM (c) images, structural schematic (d), and cycling performance (e) of the as-prepared VA-CNTs/Si arrays on the Si substrate [146].
0 10 20 30
Cycles number
-•- SnO2
-■- Fe2O3
a-Fe2O3/SnO2
Figure 12: SEM images (a, b) and structural schematic (c) of branched a-Fe2O3/SnO2 nanostructures, (d) cycling performance of a-Fe2O3/NRs arrays, pristine SnO2 NWs, and a-Fe2O3/SnO2 nanostructures at a rate of 1 Ag-1 [104].
sg 800
"0.1 Ag-1
0.5 Ag-1 0.2 Ag-
A -1 *****
3 Ag-1
4 Ag-1
10 20 30
Cycle number
Figure 13: SEM images (a, b), structural schematic (c), and rate cyclability (d) of the graphene/Sn-nanopillar nanostructures [85].
[103] fabricated by Jiang et al. via a hydrothermal method delivered reversible capacities of 690, 572, and 445mAhg_1 at the current density of 1478, 2958, and 5804 mAg^1, respectively. Zhou et al. reported that the branched a-Fe2O3/SnO2 [104] (see Figure 12) prepared by combining a vapor transport deposition and a facile hydrothermal method showed a remarkably improved initial discharge capacity of 1167 mAhg-1, which was about twice the SnO2 NWs (612mAhg"x), and a-Fe2O3 NRs (598mAhg-*). The higher capacity of the branched a-Fe2O3/SnO2 is due to that a-Fe2O3 branches provide new Li+ hosts, increase the reversible capacity, and suppress the degradation of the core SnO2.
4.2.6. Folded Heterogeneous Nanostructure Arrays. Even though complicated, the folded heterogeneous nanostruc-ture arrays are ordinarily composed of multilayered 1D nanostructure arrays embedded between 2D sheets, offering the morphological flexibility to hamper the structural collapse and efficient transport of both Li+ and electrons and leading to the excellent electrochemical performance [147]. Ji et al. reported that a multilayered graphene/Sn-nanopillar nanostructure (Figure 13), by using the self-assembly and annealing processes, retained a reversible capacity of 501 and 408mAhg_1 at a current density of 1 and 5Ag_1 after 35 cycles, respectively, which could be attributed to that both graphene and Sn served as electroactive materials, electronic conductive materials, and mechanically supporting materials [85].
5. Conclusions and Outlook
In conclusion, the recent advances in the design, fabrication, and properties of 3DSNAEs with homogeneous or heterogeneous nanoarchitectured structures for LIBs have been reviewed in detail here. Table 1 illustrates an evaluation of optimizing various electrode materials and suitable strategies to construct 3DSNAEs on various current collector substrates. From an industrial perspective, solution-based growth at low temperature and hydrothermal methods are considered to be most promising for constructing 3DSNAEs with proper electrode materials and proper electrode structures.
Evidently, the nanostructure arrays of 3DSNAEs connected to the conductive collector substrate become mechanically unstable when they are grown excessively long in the axial direction. Besides, the electrochemical performance of 3DSNAEs strongly depends on the physical/chemical properties of interface within the heterogeneous nanoarchi-tectured structures. Systematic/synergetic combining of the mechanical integrity and electrochemical kinetic properties of 3DSNAEs, therefore, will be required to the development of high-performance LIBs.
It can be seen that a large amount of research has been made in designing homogeneous or heterogeneous nano-architectured arrays in 3DSNAEs. On one hand, the hybrid structures among 1D NWs, NRs, and 2D nanosheets increase the specific energy density (especially the area and volumetric energy densities) of electrodes, by making full use of voids within the electrodes, and function simultaneously
as "stabilizers" and "buffers" to the 3DSNAEs with excellent cycling stability. On the other, the heterogeneous components concept opens a promising avenue for designing multifunctional 3DSNAEs by integrating the superiorities of each constituent. Therefore, designing the multifunctional 3DSNAEs with synergic properties by selecting suitable electrode materials and suitable structures is a bright way to address different requirements (high energy density, high conductivity, good mechanical stability, etc.) of superperformance LIBs applied in portable electronic consumer devices, electric vehicles, and large-scale electricity storage.
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