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  • Nano Express
  • Open Access

TiO2 Nanomembranes Fabricated by Atomic Layer Deposition for Supercapacitor Electrode with Enhanced Capacitance

Nanoscale Research Letters201914:92

https://doi.org/10.1186/s11671-019-2912-3

  • Received: 28 December 2018
  • Accepted: 25 February 2019
  • Published:

Abstract

TiO2 is a promising environment friendly, low cost, and high electrochemical performance material. However, impediments like high internal ion resistance and low electrical conductivity restrict its applications as electrode for supercapacitor. In the present work, atomic layer deposition was used to fabricate TiO2 nanomembranes (NMs) with accurately controlled thicknesses. The TiO2 NMs were then used as electrodes for high-performance pseudocapacitors. Experimental results demonstrated that the TiO2 NM with 100 ALD cycles had the highest capacitance of 2332 F/g at 1 A/g with energy density of 81 Wh/kg. The enhanced performance was ascribed to the large surface area and the interconnectivity in the case of ultra-thin and flexible NMs. Increased ALD cycles led to stiffer NMs and decreased capacitance. Moreover, one series of two supercapacitors can light up one light-emitting diode with a working voltage of ~ 1.5 V, sufficiently describing its application values.

Keywords

  • Atomic layer deposition
  • TiO2 nanomembranes
  • Electrode
  • Supercapacitor

Introduction

With the maturation of energy storage technology [1], supercapacitors have received vast attention due to their high power density, fast charge-discharge rate, and good cycling performance [24]. Pseudocapacitor is an important class of supercapacitors, which can deliver attractive high capacitance and energy density compared with electrochemical supercapacitors [57]. In the past few decades, the transition metal oxides (e.g., RuO2 [8], MoO2 [9], MnO2 [10], Ni/NiO [11], Co3O4 [12], and TiO2 [13]) and hydroxides [1416] were used as classic electrode materials for pseudocapacitors owing to low cost, low toxicity, multiple oxidation states [17], and great flexibility in structures and morphology. However, their thermal instability, impurity defects, and rate capability are usually limited by the inadequate conductivity to support fast electron transport required by high rates. In order to solve these problems, low-dimensional TiO2 structures (1D, 2D, 2D + 1D, and 3D) with high surface-to-volume ratio, good surface structure, great electrical and thermal stability, favorable energy band gap properties, and high dielectric constant have been engaged as promising electrode materials for supercapacitors [1822]. Especially, we think that 2D nanomembrane (NM) structures with excellent flexibility should have great potential in electrode applications. The thickness control of nanomembrane is therefore crucial in fabricating functional devices in well-defined nanoworld [23]. In addition, large-scale manufacturing of nanoscale materials is also crucial for practical applications [24]. One may note that atomic layer deposition (ALD) is a captivating technique used to construct nanodevices [25, 26]. This powerful technique can deposit thin films layer by layer with accurate thickness control and can conformally cover 3D structures with high aspect ratio [2730], and the productively can thus be greatly enhanced. In the current work, we present the fabrication of 2D TiO2 NMs with different thicknesses by performing ALD on 3D porous polymer template with large surface area [31, 32]. Microstructural characterization elucidates that the crystal structure of NM is a mixture of anatase and rutile phases. Electrochemical characterizations demonstrate that the ultra-thin and flexible NMs have the enhanced performance due to the large surface area and the interconnectivity among the NMs. The improved ion transportation causes Faradaic reaction on the surface as well as in the bulk [33], resulting in increased capacitance and energy densities.

Methods

Fabrication of TiO2 NMs

TiO2 NMs with various thicknesses (100, 200, and 400 ALD cycles) were deposited on a commercially available polyurethane sponge by using ALD technique. Tetrakis dimethylamide titanium (TDMAT) and de-ionized (DI) water were used as precursors in the presence of nitrogen (N2) gas which served as both carrier and purge gases. The flow rate of the carrier gas was 20 sccm. A typical ALD sequence includes TDMAT pulse (200 ms), N2 purge (20,000 ms), H2O pulse (20 ms), and N2 purge (30,000 ms). The precursors used were purchased from J&K Scientific Ltd., China. The precursor conformally covered the three-dimensionally porous sponge, which led to promoted productivity due to the large surface area of the template [34]. The TiO2-coated sponges were calcinated at 500 °C for 4 h in an O2 flow of 400 mL/min, and the template was completely removed. The resultant TiO2 NMs were crushed and cleaned in ethanol, hydrochloric acid (HCl), and DI water.

Preparation of Electrode

In order to fabricate high-performance supercapacitor, TiO2 NMs with 100, 200, and 400 ALD cycles were used as the active material and polytetrafluoroethylene (PTFE) was used as binder. The contents of TiO2 NMs and binder were 90 wt% and 10 wt%, respectively. A homogeneous TiO2 NMs slurry was obtained by mixing the NMs and binder with a small quantity of ethanol, and a milling process was engaged. The prepared uniform slurry was deposited onto the cleaned nickel foam and then the sample was degassed at 60 °C for 2 h in vacuum. In order to complete the electrode fabrication, the sample was pressed under 10 MPa pressure. The prepared TiO2 NMs electrode was soaked in 1 M KOH solution for 12 h to activate the electrode. The loading densities of active materials were about ~ 1.5 mg cm−2 for all electrodes. The mass of the TiO2 NMs on nickel foam was obtained by calculating the mass difference between the electrode and nickel foam [35].

Microstructural Characterization

The crystallographic structure of the TiO2 NMs was inspected by X-ray diffraction technique (XRD). The XRD patterns were recorded by using a Bruker D8A Advanced XRD with Cu Kα radiation (λ = 1.5405 Å). The morphology of TiO2 NMs was examined by scanning electron microscopy (SEM, Zeiss Sigma). The Raman spectra of the samples were carried out on a Horiba Scientific Raman spectrometer (λ = 514 nm). The elemental analysis and chemical state of the TiO2 NMs were obtained by using a PHI 5000C EACA X-ray photoelectron spectroscope (XPS), with C 1s peak at 284.6 eV as the standard signal. Atomic force microscopy (AFM, Dimension Edge, Bruker, USA) with tapping mode was used for surface topography of TiO2 NMs.

Electrochemical Characterization

Three-electrode system was utilized to study the electrochemical properties of the TiO2 NMs working electrode where Ag/AgCl and platinum foil were acted as a reference electrode and counter electrode, respectively. The cyclic voltammetry (CV), chronopotentiometry (CP), and electrochemical impedance spectroscopy (EIS) measurements were accomplished on a Chenhua CHI 660E electrochemical workstation at 25 °C in 1 M KOH aqueous solution. EIS results were obtained over the frequency range of 100 KHz to 1 Hz with an amplitude of 5 mV. The calculation methods of specific capacitances and energy/power densities are described in Additional file 1.

Results and Discussion

The preparation of TiO2 NMs is shown in Fig. 1a. The TDMAT and H2O were used as ALD precursors to deposit TiO2 on polyurethane sponge template. The reaction can be described in two half equations as follows: [36]
$$ {\displaystyle \begin{array}{l}\mathrm{Ti}{\left(\mathrm{N}{\left({\mathrm{CH}}_3\right)}_2\right)}_4+{\mathrm{TiO}}_2-{\mathrm{OH}}^{\ast}\to \mathrm{NH}{\left({\mathrm{CH}}_3\right)}_2\\ {}+{\mathrm{TiO}}_2-\mathrm{O}-\mathrm{Ti}{{\left(\mathrm{N}{\left({\mathrm{CH}}_3\right)}_2\right)}_3}^{\ast}\end{array}} $$
(1)
$$ {\displaystyle \begin{array}{l}{\mathrm{TiO}}_2-\mathrm{O}-\mathrm{Ti}{{\left(\mathrm{N}{\left({\mathrm{CH}}_3\right)}_2\right)}_3}^{\ast }+2{\mathrm{H}}_2\mathrm{O}\\ {}\to {\mathrm{TiO}}_2-{\mathrm{TiO}}_2-{\mathrm{OH}}^{\ast }+3\left(\mathrm{N}\mathrm{H}{\left({\mathrm{CH}}_3\right)}_2\right)\end{array}} $$
(2)
Fig. 1
Fig. 1

Fabrication process and morphologies of TiO2 NMs with different thicknesses. a Sketch represented fabrication process of TiO2 NMs. bd SEM images of TiO2 NMs with 100, 200, and 400 ALD cycles, respectively. Scale bars in insets are 1 μm

The total reaction can be written as:
$$ \mathrm{Ti}\Big(\mathrm{N}{\left({\mathrm{C}}_2{\mathrm{H}}_6\right)}_4+2{\mathrm{H}}_2\mathrm{O}\to {\mathrm{TiO}}_2+4{\mathrm{H}\mathrm{NC}}_2{\mathrm{H}}_6 $$
(3)
The sponge with TiO2 NM coated was then heated to high temperature. During calcination at 500 °C under oxygen atmosphere, the polymer template was converted into CO2 and left the 3D porous NM structure behind [34]. Crushing this 3D porous structure led to the fabrication of powder-like structure in white (Fig. 1a). The morphologies of TiO2 NMs with 100, 200, and 400 ALD cycles were further observed by SEM and are demonstrated in Fig. 1b–d. We found the lateral sizes of the NMs with different ALD cycles are typically around tens of microns. The thickness of TiO2 NMs fabricated in this work was probed by AFM technique and the results are presented in Additional file 1: Figure S1. The average thickness of TiO2 NMs with 100, 200, and 400 ALD cycles are ~ 15, 34, and 71 nm, respectively. With the increase of ALD cycles, TiO2 NMs is converted into a thicker and stiffer sheet. The corresponding insets in Fig. 1b–d demonstrate that the thickness of NMs is uniform, and some small creases represent the flexibility of TiO2 NM especially in the thinner cases. The NMs deposited by ALD can replicate the morphology of the original substrate (i.e., sponge) and therefore some irregular surface structures in the insets of Fig. 1c and d may originate from the template or from the calcination process [37]. Normally, TiO2 has three different crystal structures: anatase (tetragonal; space group, I41/amd), brookite (orthorhombic; space group, Pcab), and rutile (tetragonal; space group, P42/mnm) phases. Here, we carried out detailed characterization to investigate the microstructural properties of TiO2 NMs. The crystal structures of the TiO2 NMs were investigated by XRD, and the corresponding results are shown in Fig. 2a. The diffraction peaks are indexed to TiO2 with anatase and rutile structures (see Additional file 1: Figure S2), indicating the existence of the mixture phase in TiO2 NMs calcinated at 500 °C. The co-existence of both phases could be valuable for supercapacitor performance of TiO2 NMs [30, 38]. Figure 2b further demonstrates the Raman spectra of corresponding TiO2 NMs, which can also be used to identify the phases existed in the NMs. Here, five Raman peaks ascribed to anatase TiO2 are located at ~ 142 (Eg), 393 (B1g), 397 (B1g), 513 (A1g), 515 (A1g), and 634 (Eg) cm−1 [39], and they can be observed in all three samples. On the other hand, the 445 cm−1 (Eg) peak is connected with rutile phase and can be seen in all three samples but the Raman peak at 610 cm−1 (A1g) appears only in TiO2 NM with 400 ALD cycles [40]. The emergence of 610 cm−1 (A1g) peak reflects the microstructural change, which might be caused by the insufficient oxygen for the thick NM during heat treatment in oxygen [41]. This indicates that the increased number of ALD cycles has a remarkable influence on the crystal structure of the TiO2 NMs, which can be probed by XRD and Raman spectra shown in Fig. 2. The electronic configuration of the TiO2 NMs was also studied by XPS and the results are displayed in Additional file 1: Figure S3. The results prove the existence of Ti4+ in all NMs and a small shift of the peaks may be ascribed to the change in crystal structure as mentioned above. In order to study the electrochemical performance of the TiO2 NMs, three-electrode electrochemical system including a reference electrode, counter electrode, and a working electrode was operated. Here, Ag/AgCl was served as a reference electrode to control the potential difference and Pt counter electrode was engaged as an electron source to transit current towards TiO2 NMs working electrode in the presence of aqueous electrolyte (1 M KOH solution). It is worth noting that the functional voltage of supercapacitor depends on the electrolyte, and aqueous electrolyte with well electronic conductivity and high dielectric constant may be helpful in attaining higher capacitance [42]. The acquired CV and CP curves of electrodes made from TiO2 NMs with 100, 200, and 400 ALD cycles are displayed in Fig. 3a, b and Additional file 1: Figure S4. One can see that in Fig. 3a, all CV curves of three electrodes made from TiO2 NMs with different thicknesses exhibit redox peaks. The CV curve of pure nickel foam is also plotted for comparison, and no obvious peak can be observed. Generally, the appearance of redox peaks can be associated to cation interactions on the surface of the TiO2 NMs, and the interaction can be expressed as: [43]
$$ {\left({\mathrm{TiO}}_2\right)}_{\mathrm{surface}}+{\mathrm{M}}^{+}+{e}^{-}\leftrightarrow {\left({\mathrm{TiO}}_2{{}^{-}\mathrm{M}}^{+}\right)}_{\mathrm{surface}} $$
Fig. 2
Fig. 2

Micro-structural characterizations of TiO2 NMs. a XRD patterns of TiO2 NMs fabricated with 100, 200, and 400 ALD cycles. b Raman spectra of TiO2 NMs fabricated with 100, 200, and 400 ALD cycles

Fig. 3
Fig. 3

Electrochemical characterization of TiO2 NMs supercapacitor. a CV curves of pure Ni-foam, electrodes made from TiO2 NMs with 100, 200, and 400 ALD cycles. The scan rate is 10 mV/s. b CV curves of electrode made from TiO2 NMs with 100 ALD cycles, obtained at different scan rates. c CP curves of electrode made from TiO2 NMs with 100, 200, and 400 ALD cycles. The current density is 1 A/g. d CP curve of electrode made from TiO2 NMs with 100 ALD cycles, obtained at different current densities

where M+ could be H3O+or K+ in the electrolyte. The change between different oxidation states of Ti ion suggests its potential as redox electrode material. In response of fast surface Farad reaction, the CV curves of TiO2 NMs exhibit larger areas compared with that of pure Ni-foam, implying the higher specific capacitance value of TiO2 NMs. Specifically, one can see the area of the CV curves decreases with the ALD cycles, suggesting a decrease of capacitance in the case of thicker NMs, as will be further proved in following CP results. A reduction peak at ~ 0.2 V can be clearly observed in all the electrodes and is associated with intraband gap localized states [44, 45]. In addition, we also measured CV curves of electrode made from TiO2 NMs with 100 ALD at different scan rates, and the results are shown in Fig. 3b. A redox peak shifting behavior (from higher to lower potential) is connected with the change in intercalation/deintercalation of M+ ions and synergetic effect [46, 47]. Briefly, limited diffusion and charge transfer rate at a higher scan rate lead to corresponding shift [48, 49]. In order to further illustrate the charging/discharging behavior, the galvanostatic charge/discharge curves of TiO2 NMs electrodes at different current densities within a potential range of 0–0.5 V are shown in Fig. 3c, d and Additional file 1: Figure S4. The nonlinear curves of CP represent the pseudocapacitor function, which is consistent with the CV curves, and represent the Faradaic behavior. It should be noted that the discharge time of TiO2 NMs electrode with 100 ALD cycles is notably prolonged compared with TiO2 NMs electrodes with 200 and 400 ALD cycles, indicating the largest specific capacitance value. However, ultra-thin NMs electrode exhibit high gravimetric specific activity but cannot afford large current due to the limited number of active sites [50]. The extended charging/discharging times of TiO2 NMs electrodes with 100, 200, and 400 ALD cycles at current density of 1 A/g means that reduction/oxidation reactions take place (mainly on surfaces of NMs) during the process, which is the property of pseudocapacitor [51]. Figure 4 (a) shows the specific capacitances of electrodes made from TiO2 NMs with 100, 200, and 400 ALD cycles at different current densities ranging from 1 to 5 A/g. Specific capacitances of 2332, 1780, 1740, 1720, and 1690 F/g are obtained from TiO2 NMs with 100 ALD cycles, 1660, 1300, 1182, 1104, and 1040 F/g from TiO2 NMs with 200 ALD, and 1094, 848, 732, 672, and 630 F/g from TiO2 NMs with 400 ALD cycles. In previous literature, Yang et al. [43] prepared the TiO2/N-doped graphene composite structure with a capacitance of 385.2 F/g at 1 A/g and 320.1 F/g at 10 A/g. Zhi et al. [52] reported a specific capacitance of 216 F/g for TiO2 nanobelts with nitrogen doping. Di et al. [53] fabricated TiO2 nanotubes decorated with MnO2 nanoparticles and a specific capacitance of 299 F/g at a current density of 0.5 A/g was obtained. Obviously, the capacitance of the electrode made from current TiO2 NMs is much higher. Moreover, the energy and power density relation of the three electrodes are shown in Fig. 4b and Additional file 1: Table S1. Energy density is the capacity of energy storage devices and power density is their ability to deliver it, and both are the key parameters used to evaluate the electrochemical performance of supercapacitors. Vividly, when current density increases from 1 to 5 A/g, TiO2 NMs electrode with 100 ALD cycles possesses a high energy density of 81–57 Wh/kg compared to 59–36 Wh/kg of TiO2 NMs electrode with 200 ALD cycles and 38–21 Wh/kg of TiO2 electrode NMs with 400 ALD cycles, while the power density increases from 250 to 1250 W/kg (Fig. 4b). The high performance might be due to the mixture of anatase and rutile phases (Fig. 2) as this leads to surface passivation and increased ion transportation [5456]. In addition, the enlarged surface area of the TiO2 NMs and interconnectivity among the NMs also cause the enhancement in ions transportation. On the other hand, we believe that the decrease in electrochemical performance with the increasing ALD cycles is mainly due to the decreased NM/electrolyte interface area if the masses of the active materials are the same. Moreover, the TiO2 NMs with more ALD cycles (i.e., thickness) is stiffer and flat (see Fig. 1), and therefore, the overlap between the NMs is obvious. This may limit the surface access for electrolyte ions, resulting in dead volume, high resistance, and reduced capacitance [57]. In addition, with the increase of current densities, the diffusion rate of electrolyte might not be enough to satisfy the electrochemical reaction of electrode material, and therefore, a decrease of capacitance with current density can be observed in Fig. 4a [39, 40]. In order to further reveal the electrochemical properties of the current TiO2 NMs electrodes, EIS characterizations was carried out because EIS can provide the information about electrode-electrolyte and electrode internal resistance [58]. Figure 4c demonstrates the EIS results of all three electrodes, and the horizontal intercept indicates the internal resistance of pseudocapacitor. It is clearly observed that TiO2 NMs electrode with 400 ALD cycles possesses high internal resistance as compared to TiO2 NMs electrodes with 200 and 100 ALD cycles. We consider that the increased resistance of TiO2 NMs electrode with 400 ALD cycles is mostly by reason of increased NM thickness since the TiO2 has relatively large resistivity [39, 48]. The TiO2 NMs with 100 ALD cycles exhibits the lowest internal resistance compared with others because the large surface area allows the better ions passage [59] and flexibility of thin NM improves the interlayer connection with decreased resistivity. All these results demonstrate that thin TiO2 NMs with high electroactivity are promising electrode materials for high-performance pseudocapacitor. In order demonstrate the potential application of TiO2 NMs supercapacitor, four electrodes made from TiO2 NMs with 100 ALD cycles were assembled into two symmetrical supercapacitors, i.e., each supercapacitor consisted of two electrodes of TiO2 NMs with 100 ALD cycles. The two supercapacitors were connected in series and then charged at 5 A/g current density to 0.5 V. Afterwards, they were used to light up a red LED (light-emitting diode) with working voltage of ~ 1.5 V and the LED emitted light for ~ 1 min (see Fig. 4d and Additional file 2: Video S1). The cycle stability of the electrode made from TiO2 NMs with 100 ALD cycles was also studied and the results are shown in Additional file 1: Figure S5. A capacitance retention of 80.98% is observed after cycling at 5 A/g for 40 charge/discharge cycles, suggesting a less interaction of electrolyte ions with electrode surface after repeated cycles. We believe that the performance of the NMs electrode might be further promoted if the conductivity of the NMs is increased. With the help of the ALD technique, the conductivity of the NMs can be increased by fabricating multi-layered NMs where materials with high conductivity are incorporated. More works are currently in progress.
Fig. 4
Fig. 4

Performance comparison of TiO2 NMs electrodes. a Specific capacitances of the TiO2 NM electrodes at various current densities. b Ragone plot of TiO2 NMs electrodes with 100, 200, and 400 ALD cycles. c Nyquist plot of three TiO2 NMs electrodes. d A photo showing that two supercapacitors in series can lighten up a red LED

Conclusion

In summary, we have fabricated TiO2 NMs for electrodes of supercapacitor, and the electrochemical performance of the NMs was studied in detail. The TiO2 NM electrode demonstrates increased capacitance with deceased NM thickness. At a current density of 1 A/g, the specific capacitance of 2332 F/g is obtained for TiO2 NM with 100 ALD cycles, and the corresponding energy density is calculated to be 81 Wh/kg. The enhancement of the performance is mainly attributed to the fabrication strategy and the ultra-thin feature of NMs, because the large surface area and short diffusion path of NMs facilitate ion transport through electrode/electrolyte interface. The interconnectivity among the NMs also remarkably enhances the ion transportation in the electrode. We also demonstrate that two supercapacitors connected in series can power a LED, suggesting the application potential of TiO2 NMs supercapacitor. The current facile design opens the way to build NMs electrodes for next-generation wearable energy storage devices at low-cost. However, for practical applications of NM-based structures in future supercapacitors, further studies are required.

Abbreviations

AFM: 

Atomic force microscopy

ALD: 

Atomic layer deposition

CP: 

Chronopotentiometry

CV: 

Cyclic voltammetry

DI: 

De-ionized water

EIS: 

Electrochemical impedance spectroscopy

LED: 

Light-emitting diode

NMs: 

Nanomembranes

PTFE: 

Polytetrafluoroethylene

SEM: 

Scanning electron microscopy

TDMAT: 

Tetrakis dimethylamide titanium

XPS: 

X-ray photoelectron spectroscopy

XRD: 

X-ray diffraction spectrometer

Declarations

Acknowledgement

The authors are grateful to Dr. Yingchang Jiang, Zhao Zhe, Dr. Atif Zahoor, Dr. Shahid Rasool, Dr. Alexander A Solovev and Dr. David H. Gracias for their helpful discussion and guidance.

Funding

This work is supported by the Natural Science Foundation of China (Nos. U1632115 and 61805042), Science and Technology Commission of Shanghai Municipality (No. 17JC1401700), and the Changjiang Young Scholars Program of China. Part of the work is also supported by the National Key Technologies R&D Program of China (No. 2015ZX02102-003).

Availability of Data and Materials

The datasets generated during and/or analyzed during the current study are available from the corresponding author on request.

Authors’ Contributions

FN carried out the experiment, analyzed the data, and wrote the manuscript. SN helped in analyzing the data. YTZ and DRW helped in the sample characterization. JZ, YFM, and GSH provided the research directions and revised the manuscript. All authors read and approved the final manuscript.

Competing Interests

The authors declare that they have no competing interests.

Publisher’s Note

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Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

(1)
Department of Materials Science, Fudan University, 220 Handan Road, Shanghai, 200433, People’s Republic of China
(2)
State Key Laboratory for Modification of Chemical Fibers and Polymer Material Science and Engineering, Donghua University, Shanghai, 201620, People’s Republic of China
(3)
College of Science, Donghua University, Shanghai, 201620, People’s Republic of China

References

  1. Armaroli N, Balzani V (2011) Towards an electricity-powered world. Energy Environ Sci 4:3193–3222View ArticleGoogle Scholar
  2. Yu M, Han Y, Cheng X, Hu L, Zeng Y, Chen M, Cheng F, Lu X, Tong Y (2015) Holey tungsten oxynitride nanowires: novel anodes efficiently integrate microbial chemical energy conversion and electrochemical energy storage. Adv Mater 27:3085–3091View ArticleGoogle Scholar
  3. Kötz R, Carlen M (2000) Principles and applications of electrochemical capacitors. Electro Acta. 45:2483View ArticleGoogle Scholar
  4. Burke A (2000) Ultracapacitors: why, how, and where is the technology. J Power Sources 91:37View ArticleGoogle Scholar
  5. Conway BE, Birss V, Wojtowicz J (1997) The role and utilization of pseudocapacitance for energy storage by supercapacitors. J Power Sources 66:1–14View ArticleGoogle Scholar
  6. Miller J, R Simon P (2008) Electrochemical capacitors for energy management. Science 321:651–652View ArticleGoogle Scholar
  7. Meng X, Deng J, Zhu J, Bi H, Kan E, Wang X (2016) Cobalt sulfide/graphene composite hydrogel as electrode for high-performance pseudocapacitors. Sci Rep 6:21717–21725View ArticleGoogle Scholar
  8. Trasatt S, Buzzancai G (1971) Ruthenium dioxide: a new interesting electrode material. Solid state structure and electrochemical behaviour. J Electroanal Chem 29:A1-A5Google Scholar
  9. Yao B, Huang L, Zhang J, Gao X, Wu J, Cheng Y, Xiao X, Wang B, Li Y, Zhou J (2016) Flexible transparent molybdenum trioxide nanopaper for energy storage. Adv Mater 28:6353–6358View ArticleGoogle Scholar
  10. Huang ZH, Song Y, Feng DY, Sun Z, Sun XQ, Liu XX (2018) High mass loading MnO2 with hierarchical nanostructures for supercapacitors. ACS Nano 12:3557–3567View ArticleGoogle Scholar
  11. Liu FG, Wang XB, Hao J, Han S, Lian J, Jiang Q (2017) High density arrayed Ni/NiO core-shell nanospheres evenly distributed on graphene for ultrahigh performance supercapacitor. Sci Rep 7:17709–17718View ArticleGoogle Scholar
  12. Duan Y, Hu T, Yang L, Gao J, Guo S, Hou M, Ye X (2019) Facile fabrication of electroactive microporous Co3O4 through microwave plasma etching for supercapacitors. J of Alloys and Comp 771:156–161View ArticleGoogle Scholar
  13. Lu X, Wang G, Zhai T, Yu M, Gan J, Tong Y, Li Y (2012) Hydrogenated TiO2 Nanotube Arrays for Supercapacitors. Nano Lett 12:1690−1696.Google Scholar
  14. Deng T, Lu Y, Zhang W, Sui M, Shi X, Wang D, Zheng W (2018) Inverted design for high-performance supercapacitor via co (OH)2-derived highly oriented MOF electrodes. Adv Energy Mat 8:1702294–1702300View ArticleGoogle Scholar
  15. Wang HL, Casalongue HS, Liang Y, Dai HJ (2010) Ni (OH)2 nanoplates grown on graphene as advanced electrochemical pseudocapacitor materials. J Am Chem Soc 132:7472–7477View ArticleGoogle Scholar
  16. Xia XH, Tu JP, Zhang YQ, Chen J, Wang XL, Gu CD, Guan C, Luo JS, Fan HJ (2012) Porous hydroxide nanosheets on preformed nanowires by electrodeposition: branched nanoarrays for electrochemical energy storage. Chem Mater 24:3793–3799View ArticleGoogle Scholar
  17. Zhao X, Sánchez BM, Dobson PJ, Grant PS (2011) The role of nanomaterials in redox-based supercapacitors for next generation energy storage devices. Nanoscale. 3:839–855View ArticleGoogle Scholar
  18. Ozkan S, Nguyen NT, Hwang I, Mazare A, Schmuki P (2017) Highly conducting spaced TiO2 nanotubes enable defined conformal coating with nanocrystalline Nb2O5 and high-performance supercapacitor applications. Small. 13:1603821View ArticleGoogle Scholar
  19. Banerjee AN, Anitha VC, Joo SW (2017) Improved electrochemical properties of morphology controlled titania/titanate nanostructures prepared by in-situ hydrothermal surface modification of self-source Ti substrate for high performance supercapacitors. Sci Rep 7:13227–13246View ArticleGoogle Scholar
  20. Ke QQ, Zheng M, Liu HJ, Guan C, Mao L, Wang J (2015) 3D TiO2@Ni (OH)2 core-shell arrays with tunable nanostructure for hybrid supercapacitor application. Sci Rep 5:13940–13950View ArticleGoogle Scholar
  21. Jiang L, Ren ZF, Chen S, Zhang Q, Lu X, Zhang HP, Guojiang Wan GJ (2018) Bio-derived three-dimensional hierarchical carbon-graphene-TiO2 as electrode for supercapacitors. Sci Rep 8:4412–4120View ArticleGoogle Scholar
  22. Kim C, Kim S, Lee J, Kim J, Yoon J (2015) Capacitive and oxidant generating properties of black-colored TiO2 nanotube array fabricated by electrochemical self-doping. ACS Appl Mater Inter 7:7486–7491View ArticleGoogle Scholar
  23. Huang G, Mei YF (2018) Assembly and self-assembly of nanomembrane materials—from 2D to 3D. Small 14:1703665Google Scholar
  24. Li XJ, Liu W, Wang J, Rozen I, He S, Chen C, Kim GH, Lee HJ, Lee H-B-R, Kwon S-H, Li LT, Li QL, Wang J, Mei YF (2017) Nanoconfined atomic layer deposition of TiO2/Pt nanotubes: toward ultrasmall highly efficient catalytic nanorockets. Adv Funct Mater 27:1700598Google Scholar
  25. George SM (2010) Atomic layer deposition: an overview. Chem Rev 110:111–131View ArticleGoogle Scholar
  26. Johnson RW, Hultqvist A, Bent SF (2014) A brief review of atomic layer deposition: from fundamentals to applications. Mater Today 17:236–246View ArticleGoogle Scholar
  27. George SM, Ott AW, Klaus JW (1996) Surface chemistry for atomic layer growth. J Phys Chem 100:13121–13131View ArticleGoogle Scholar
  28. Ritala M, Leskela M. Handbook of thin film materials; Nalwa, H. S., Ed.; Academic Press: San Diego. 2001Google Scholar
  29. Kim H (2011) Characteristics and applications of plasma enhanced-atomic layer deposition. Thin Solid Films 519:6639–6644View ArticleGoogle Scholar
  30. Boukhalfa S, Evanoff K, Yushin G (2012) Atomic layer deposition of vanadium oxide on carbon nanotubes for high-power supercapacitor electrodes. Energy Environ Sci 5:6872–6879View ArticleGoogle Scholar
  31. Abendroth B, Moebus T, Rentrop S, Strohmeyer R, Vinnichenko M, Weling T, Stöcker H, Meyer DC (2013) Atomic layer deposition of TiO2 from tetrakis(dimethylamino) titanium and H2O. Thin Solid Films 545:176–182View ArticleGoogle Scholar
  32. Reiners M, Xu K, Aslam N, Devi A, Waser R, Eifert SH (2013) Growth and crystallization of TiO2 thin films by atomic layer deposition using a novel amido guanidinate titanium source and tetrakis-dimethylamido-titanium. Chem Mater 25:2934–2943View ArticleGoogle Scholar
  33. Sun X, Xie M, Wang GK, Sun HT, Cavanagh AS, Travis JJ, George SM, Liana J (2012) Atomic layer deposition of TiO2 on graphene for supercapacitors. J of the Electro Soc 159:364–369View ArticleGoogle Scholar
  34. Pan SQ, Zhao Y, Huang GS, Wang J, Baunack S, Gemming T, Li ML, Zheng L, Schmidt OG, Mei YF (2015) Highly photocatalytic TiO2 interconnected porous powder fabricated by sponge-templated atomic layer deposition. Nanotech. 26:364001–364006View ArticleGoogle Scholar
  35. Chen H, Hu LF, Chen M, Yan Y, Wu L (2014) Nickel-cobalt layered double hydroxide nanosheet for high-performers supercapacitor electrode materials. Adv Funct Mater 24:934–942View ArticleGoogle Scholar
  36. Xie Q, Jiang YL, Detavernier C, Deduytsche D, Meirhaeghe RLV, Ru GP, Li BZ, Qu X (2007) Atomic layer atomic layer deposition of TiO2 from tetrakis-dimethyl-amido titanium or Ti iopropxide precursors and H2O. J of Appl Phy 102:083521–083527View ArticleGoogle Scholar
  37. Edy R, Huang GS, Zhao Y, Zhang J, Mei YF, Shi JJ (2016) Atomic layer deposition of TiO2-nanomembrane-based photocatalysts with enhanced performance. AIP Adv 6:115113–115121View ArticleGoogle Scholar
  38. Huang S, Zhang L, Lu X, Liu L, Sun X, Yin Y, Oswald S, Zou Z, Ding F, Schmidt OG (2017) Tunable pseudocapacitance in 3D TiO2−δ nanomembranes enabling superior lithium storage performance. ACS Nano 11:821–830View ArticleGoogle Scholar
  39. Salari M, Konstantinov K, Liu HK (2011) Enhancement of the capacitance in TiO2 nanotubes through controlled introduction of oxygen vacancies. J Mater Chem 21:5128–5133View ArticleGoogle Scholar
  40. Rezaee M, Khoie SMM, Liu KH (2011) The role of brookite in mechanical activation of anatase-to-rutile transformation of nanocrystalline TiO2: an XRD and Raman spectroscopy investigation. Cryst Eng Comm 13:5055–5061View ArticleGoogle Scholar
  41. Peng X, Chen A (2004) Aligned TiO2 nanorod arrays synthesized by oxidizing titanium with acetone. J Mater Chem 14:2542–2548View ArticleGoogle Scholar
  42. Beati AAGF, Reis RM, Rocha RS, Lanza MRV (2012) Development and evaluation of a pseudoreference Pt/Ag/AgCl electrode for electrochemical systems. Ind Eng Chem Res 51:5367–5371View ArticleGoogle Scholar
  43. Yang SH, Lin Y, Song XF, Zhang P, Gao L (2015) Covalently coupled ultrafine H-TiO2 nanocrystals/nitrogen-doped graphene hybrid materials for high-performance supercapacitor. ACS Appl Mater Interfaces 7:17884–17892View ArticleGoogle Scholar
  44. Santiago FF, Mora-Sero I, Garcia-Belmonte G, Bisquert J (2003) Cyclic voltammetry studies of nanoporous semiconductors. Capacitive and reactive properties of nanocrystalline TiO2 electrodes in aqueous electrolyte. J Phys Chem B 107:758–768View ArticleGoogle Scholar
  45. Wu H, Li D, Zhu X, Yang C, Liu D, Chen X, Song Ye LL (2014) High-performance and renewable supercapacitors based on TiO2 nanotube array electrodes treated by an electrochemical doping approach. Electro Acta 116:129–136View ArticleGoogle Scholar
  46. Li M, Zhou M, Wen QZ, Zhang XY (2017) Flower-like NiFe layered double hydroxides coated MnO2 for high-performance flexible supercapacitors. J of Ener Stor 11:242–248View ArticleGoogle Scholar
  47. Xiao J, Wan L, Yang S, Xiao F, Wang S (2014) Design hierarchical electrode with highly conductive NiCo2S4 nanotube performance arrays grown on carbon fiber paper for high-performance Pseudocacpcitors. Nano Lett 14:831–838View ArticleGoogle Scholar
  48. Liu LJ, Chen M, Zhang L, Jiang J, Yan J, Huang Y, Lin J, Fan JH, Shen XZ (2014) A flexible alkaline rechargeable Ni/Fe battery based on graphene foam/carbon nanotubes hybrid film. Nano Lett 14:7180–7187View ArticleGoogle Scholar
  49. Liu B, Liu B, Wang Q, Wang X, Xiang Q, Chen D, Shen G (2013) New energy storage option: toward ZnCo2O4 nanorods/nickel foam architectures for high-performance supercapacitors. ACS Appl Mater Inter. 5:10011–10017View ArticleGoogle Scholar
  50. Tang Z, Tang CH, Gong H (2012) A high energy density asymmetric supercapacitor from nano-architectured Ni (OH)2/carbon nanotube electrodes. Adv Funct Mater 22:1272–1278View ArticleGoogle Scholar
  51. Zhang Q, Xu WW, Sun J, Pan ZH, Zhao JX, Wang X, Zhang J, Man P, Guo JB, Zhou ZY, He B, Zhang ZX, Li QW, Zhang YG, Xu L, Yao Y (2017) Constructing ultrahigh-capacity zinc−nickel−cobalt oxide @ Ni(OH)2 Core−Shell nanowire arrays for high-performance coaxial fiber-shaped asymmetric supercapacitors. Nano Lett 17:7552–7560View ArticleGoogle Scholar
  52. Zhi J, Zhao W, Lin TQ, Huang F (2017) Boosting supercapacitor performance of TiO2 nanobelts by efficient nitrogen doping. Chem Electro Chem 4:2328–2335Google Scholar
  53. Di J, Fu XC, Zheng H, Jia Y (2015) H-TiO2/C/MnO2 nanocomposite materials for high-performance supercapacitors. J Nano Res 17:255–266View ArticleGoogle Scholar
  54. Barnard SA, Curtiss AL (2005) Prediction of TiO2 nanoparticle phase and shape transitions controlled by surface chemistry. Nano Lett 5:1261–1266View ArticleGoogle Scholar
  55. Barnard SA, Zapol P (2004) Predicting the energetics, phase stability, and morphology evolution of faceted and spherical anatase nanocrystals. J Phys Chem B 108:18435–18440View ArticleGoogle Scholar
  56. Barnard SA, Zapol P, Curtiss AL (2005) Anatase and rutile surfaces with adsorbates representative of acidic and basic conditions. Surf Sci 582:173–188View ArticleGoogle Scholar
  57. Hercule MK, Wei Q, Khan MA, Zhao LY, Tian CX, Mai QL (2013) Synergistic effect of hierarchical nanostructured MoO2/co (OH)2 with largely enhanced pseudocapacitor cyclability. Nano Lett 13:5685–5691View ArticleGoogle Scholar
  58. Carrara S, Bavastrello V, Ricci D, Stura E, Nicolini C (2005) Improved nano composite materials for biosenser applications investigated by electrochemical impedance spectroscopy. Sens Actu B 109:221–226View ArticleGoogle Scholar
  59. Zhao H, Liu L, Vellacheri R, Lei Y (2017) Recent advances in designing and fabricating self-supported nanoelectrodes for supercapacitors. Adv Sci 4:1700188–1700222View ArticleGoogle Scholar

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