Applied Nanoscience

, Volume 6, Issue 4, pp 511–519 | Cite as

Mixed-phase bismuth ferrite nanoflake electrodes for supercapacitor application

  • Vijaykumar V. Jadhav
  • Manohar K. Zate
  • Shude Liu
  • Mu. Naushad
  • Rajaram S. ManeEmail author
  • K. N. HuiEmail author
  • Sung-Hwan Han
Open Access
Original Article


Nanoflake bismuth ferrite thin film was synthesized by means of electrodeposition technique at room temperature. The morphology and phase evaluation of the synthesized electrode were analyzed using scanning electron microscopy, X-ray diffraction, Raman spectroscopy, and surface wettability techniques. Specifically, the bismuth ferrite nanoflake electrode exhibited high specific capacitance of 72.2 F g−1 at a current density of 1 A g−1, and high rate capability with 37 % retention of capacitance even up to 20A g−1, and excellent cycling stability with 82.8 % retention of the initial capacitance after 1500 charge/discharge cycles, supporting that the bismuth ferrite thin-film electrode could be a potential candidate for supercapacitor application.


Electrodeposition Nanostructure Ferrite Electrochemical supercapacitor 


Now-a-days, fast-growing market for portable electronic devices such as mobile phones, laptops, notebook computers, uninterruptible power supply, and the development of hybrid electric vehicles, etc., is increasing and there is an urgent demand for environmental-friendly high-power energy storage resources. Also rapid growth of research in the field of electrochemical energy storage systems has been driven by the increased development of nanostructured materials. Electrochemical supercapacitors have attracted great attention because of their ability to deliver high power and energy densities with outstanding cycling stability. A supercapacitor is an assuring energy storage device, which can function as a gap-bridging device between batteries and conventional capacitors (Chu and Majumdar 2012; Winter and Brodd 2004; Zhai et al. 2011). Supercapacitive performance of a material either in the form of a thin-film or of a pallet, used as an electrode can be assayed by cyclic-voltammetry (CV) and galvanostatic charge–discharge measurements. An electrode is judged by its specific capacitance value and the number of charge–discharge cycles it withstands, maintaining the constancy of capacitance. This brings forth the search for a wide variety of materials. In general, transition metal oxides, including RuO2, MnO2, NiO, Co3O4, SnO2, ZnO, TiO2, V2O5, CuO, Fe2O3, and WO3 (Lang et al. 2011; Athoue et al. 2008; Yan et al. 2010; Chen et al. 2012; Luo et al. 2014; Liu et al. 2014; Sathiya et al. 2011; David et al. 2014; Brezesinski et al. 2009; Wang et al. 2013; Liang et al. 2010; Xia et al. 2014; Kang et al. 2013; Yu et al. 2014), etc., have demonstrated high specific capacitance values with their redox reaction behaviors.

Ferrites, a class of metal oxide-based materials, have been attracting great attention in energy storage device due to their important applications in electronic materials industries. Most fascinating applications of ferrite materials include antenna rod, transformer core, recording head, loading coil, memory, and microwave devices, etc. (Petzold 2003; Niesen and De Guire 2001; Yoshimura et al. 2000). The present day electronic industries move constantly toward miniaturization of devices, and development of new materials to replace the existing ones when their inherent technological limits have been reached. The field of smart multiferroics is the top research topic (Schileo 2013; Kuo 2013). Bismuth ferrite (BFO), one of the very few multiferroics with a simultaneous coexistence of parameters of both ferroelectric and antiferromagnetic orders in perovskite structure, has been attracting great attention over the past several decades. Potential applications of BFO in the memory devices, such as sensors, spintronic devices, satellite communications, optic filters, and smart devices, etc., are greatly limited due to its low insulation resistance caused by the reduction of Fe3+ species to Fe2+ and in oxygen vacancies for charge compensation (Wang et al. 2004; Martin 2010; Cheong and Mostovoy 2007). The preparation of single-phase BFO without impurities is a critical task due to its narrow temperature stability range (Jaiswal et al. 2010). Using conventional solid-state reaction routes, the preparation of BFO material faces following difficulties:
  1. (a)

    It is difficult to develop the pure phase of BFO, i.e., BiFeO3, as while forming BFO, other thermodynamically more stable phases such as Bi2Fe4O9, Bi46Fe2O72, Bi25FeO40, Bi24Fe2O39, and Bi36Fe2O57, etc, are generally dominant.

  2. (b)

    In general, the platinum crucible is needed for its preparation, which can be used only for three or four times. This increases the sample preparation cost, and,

  3. (c)

    during the deposition, the substrate must be placed at the elevated temperatures; therefore, this causes restrictions on the selection of the substrate material.


Single-phase BFO powder was prepared by oxide-mixing technique followed by leaching with dilute nitric acid to eliminate unreacted impurity phases (Kumar et al. 2000). Palkar and Pinto (2002) have reported the synthesis of highly resistive thin film of pure BFO phase using pulsed laser-deposition method. Epitaxial growth of BFO phase, i.e., Bi3Fe5O12, has been prepared by a reactive ion beam sputtering technique by Adachi et al. (2000). BFO nanostructures including nanofibers (Mohan and Subramanian 2013), nanowires (Das et al. 2013; Gao et al. 2006), nanorods (Xie et al. 2008), nanoparticles (Chen et al. 2006; Biasotto et al. 2011; Jadhav et al. 2013), microcubes, and nanoplates (Waghmare et al. 2012) have already been reported. These nanostructures are expected to offer better efficiency owing to their large surface areas giving rise to high values of specific capacitance. Electrodeposition is a powerful and interesting methodology that can be applied in numerous fields for synthesizing thin metal oxide/chalcogenide thin films or coatings. It has been used for the preparation of thin and thick films of iron group metal oxides at relatively low temperatures (Sartale et al. 2004; Mo et al. 2000; Gujar et al. 2006). Lokhande et al. (2007) obtained BFO films with a specific capacitance of 81 F g−1 using electrodeposition method. Dutta et al. (2013) reported remarkably a high value of specific capacitance of 450 F g−1 for BFO nanorods prepared by a wet chemical template method.

In the present study, BFO structures of mixed phases were synthesized onto conducting substrate using electrodeposition technique at room temperature. These electrodes were further envisaged for their structural elucidation and morphological confirmation studies. Different preparative parameters including the effective potential window, the pH of bath composition, and the temperature effects were optimized so as to get optimal supercapacitive performance. The mechanisms of reduction and oxidation reactions in the electrolyte were studied for different current densities and CV curves. The effects of bismuth nitrate and ferric nitrate concentrations on structural, morphological, surface wettability, and supercapacitive properties were explored. The effects of electrolyte concentration and scan rate on electrochemical properties of BFO were also investigated. In addition, charging–discharging, Raman analysis, and impedance characteristics of BFO electrodes were studied.


Sample synthesis and characterizations

BFO thin film electrodes were prepared using analytic grade chemicals and double-distilled water. The bath solution was made up of 0.2 M bismuth (III) nitrate (Bi (NO3)3·5H2O), and 0.2 M ferric (III) nitrate (Fe (NO3)3) with 0.2 M tartaric acid (C4H6O6) as a complexing agent, and the pH value of ~12 was maintained through the addition of sodium hydroxide (NaOH) aqueous solution. BFO thin films were electrodeposited onto precleaned SS substrate under galvanostatic mode using CP at 3 mA for 300 s. At room temperature, electrodeposited sample was black in color. These films were then air annealed at 400, 500, and 600 °C temperatures for 2 h. Reddish films were seen with naked eyes on the SS substrate after annealing at 400 and 500 °C. At 600 °C, the sample again turned black in color. The mass of active BFO electrode material was around 1 mg cm−2.

Mixed-phase BFO electrodes were examined for their morphologies and structures. X- ray diffractometer (Rigaku D/MAX 2500 V, Cu Kα, λ=1.5418 Å) was used for obtaining X-ray diffraction (XRD) spectra, and for evaluating surface morphologies, field-emission scanning electron microscopy (FE-SEM, Hitachi S-4200) images were recorded. Raman shift measurement was taken in order to confirm ferrite phase transformation with the increasing temperature. Contact angle measurements on as-deposited film electrode surfaces were carried out by sessile drop method, in which water drop was observed through a microscope-coupled goniometer (Phoenix 150, Surface Electro Optics, Korea). For electrochemical measurements, 1 × 1 cm2 was defined as the active electrode surface area for each measurement in the presence of platinum (Pt) as counter electrode and Ag/AgCl as reference electrode in 1 M NaOH. A frequency range of 0.01 Hz–1.5 MHz and an amplitude of 50 mV were applied during the EIS analysis.

Results and discussion

Figure 1 shows digital photoimages of BFO electrodes deposited onto SS substrate by means of electrodeposition method at room temperature, which were further annealed at 400, 500, and 600 °C temperatures. As seen in Fig. 1, the as-deposited films were black in color. After annealing at 400 °C, the films turned reddish. At 500 °C, the films turned into reddish yellow, and finally, at 600 °C, the film surface was again black in appearance.
Fig. 1

Digital photoimages of mixed phase bismuth ferrites for different annealing temperatures

The XRD spectra of BFO electrodes synthesized and annealed at 400, 500, and 600 °C temperatures are presented in Fig. 2. BFO film annealed at 600 °C exhibited intense reflection peaks which correspond to Bi2F4O9 structure. Most of the obtained (201), (211), (002), (221), (310), and (142) peaks were closely matching with Bi2F4O9 phase of BFO (JCPDS card no. 25-0090). The lattice parameters were a =7.96 Å, b =8.44 Å, c =5.99 Å with orthorhombic Bi2F4O9 type crystal structure. Secondary BiFeO3 phase of BFO was noticed at 600 °C due to occurrence of (012), (202), (113), (104), (300), (312) peaks (JCPDS Card no. 20-0169) in XRD pattern. The lattice parameters of BiFeO3 were a =b =5.58 Å, c =6.93 Å with rhombohedral structure (Zheng et al. 2012). Ternary phase Bi25FeO40 was also confirmed in accordance with JCPDS card no. 46-0416 as there were only (211), (332), and (541) peaks. From XRD pattern, it was clear that Bi2F4O9 phase was more dominant than BiFeO3 phase. Only two peaks were of Bi25FeO40. Hence, it was concluded that at 600 °C, BFO phase cannot be supposed to have high crystallinity. Along with the formation of primary phase of BFO (BiFeO3), secondary phase and ternary phases were also emerged (Singh et al. 2008; Perejon et al. 2014; Bernardo et al. 2011) as a function of annealing temeparture.
Fig. 2

XRD spectra of BFO electrodes annealed at 400, 500, and 600 °C

Surface morphologies of BFO electrodes annealed at 400, 500, and 600 °C for 2 h are shown in Fig. 3. It was concluded that by changing the electrodeposition composition/condition, the structural morphology can be greatly altered. From the FE-SEM imaging, the BFO electrode annealed at 400 °C revealed irregular flake-like structure. A few smaller crystallites of irregular dimensions were found on the surfaces. Morphology of BFO electrode annealed at 500 °C showed a smooth and polished-type structure. Moreover, flakes were smaller in dimensions. A few numbers of smaller crystallites were seen on these flakes. At 600 °C annealing temperature, these flakes were polished-type structure. There were no small crystallites seen over the flakes as seen in other cases. Figure 3 shows the EDX pattern of BFO electrode deposited onto SS substrate, annealed at 600 °C for 2 h, and the elemental analyses carried out for Bi, Fe, and O. From the EDX pattern, the presence of Bi, Fe, and O elements in the electrodeposited BFO product in the ratio of 1:2:3 was confirmed. Figure 4 shows Raman spectra with vibrational modes at 616, 663, 830, 821, 852, and 1327 cm−1. From Raman analysis it was clear that at 600 °C, BFO phase formation was confirmed. The presence of only one Raman mode at 400 and 500 °C supported the fact that the temperatures below 500 °C were not adequate for the formation of ferrite structure. For the BFO obtained at 600 °C, five Raman modes appeared suggesting the formation of ferrite structure.
Fig. 3

FE-SEM images of BFO electrodes annealed at 400, 500, and 600 °C and EDX spectra at 600 °C

Fig. 4

Raman spectra of BFO electrodes annealed at 400, 500, and 600 °C

The surface microstructure plays a vital role in the wetting properties of materials. The wetting behavior of surfaces is governed by both their chemical composition and geometric microstructure. If the surface wettability is high, contact angle (θ) will be small, and the surface is hydrophilic. On the contrary, if the wettability is low, θ will be large, and the surface is hydrophobic. Figure 5 presents water contact angle measurements on BFO electrode surfaces annealed at 400, 500, and 600 °C temperatures. Due to change in surface morphology, the contact angle was decreased from 86.21° to 58.48°. With the increasing annealing temperature, water contact angle value was decreased. Lower contact could be beneficial for achieving enhanced specific capacitance (Mane et al. 2007; Sun et al. 2001; Conway and Pell 2002).
Fig. 5

Contact angle measurements on SS and BFO surfaces annealed at various temperatures

Cyclic voltammetry (CV) measurement was employed to explore the BFO electrodes for electrochemical supercapacitor application with NaOH electrolyte of different concentrations in a conventional three-electrode system.

Effect of scan rate on electrochemical supercapacitor performance of BFO electrode was studied in 0.25, 0.5, 0.75, 1, 1.5, and 2 M NaOH electrolyte concetrations at the constant scan rate 10 mV s−1. Figure 6 represents CV curves of BFO electrodes in NaOH electrolyte of different concentrations. From the results, it was concluded that with the increasing concentration of NaOH electrolyte from 0.25 to 2 M, the SC value of BFO was increased. It was found that the BFO electrode annealed at 600 °C exhibited maximum current density which could be attributed to the formation of complete ferrite structure. This electrode was scanned for different scan rates in 2 M NaOH, and the results are shown in Fig. 7a. With the scan rate being increased from 10 to 1000 mV s−1, the SC value of BFO electrode was found to decrease from 101.63 to 5.65 F g−1, indicating that at lower scan rates, inner and outer sites were more active, and thus, full utilization of BFO electrode in NaOH electrolyte solution occured. Hence, this might help to increase the SC of BFO electrode at lower scan rate. At higher scan rates, only outer sites could be more active than inner sites which were unable to participate in the redox reaction in the electrolyte solution (Subramanian et al. 2004; Wang et al. 2012).
Fig. 6

CV curves of BFO electrode in; a 0.25 M, b 0.5 M, c 0.75 M, d 1 M, e 1.5 M, f 2 M NaOH

Fig. 7

a Effect of scan rate on SC value of BFO electrode. b Galvanostatic charge–discharge curves of the BFO at different current densities. c Specific capacitance under different current densities. d Capacitance retention for BFO at 1500 cycles. e EIS measurement of BFO electrode

To further investigate electrochemical performances of the nanoflake BFO electrode, we perform galvanostatic charge–discharge (GCD) curves at various current densities in an electrochemical window from −0.8 to 0.2 V (Fig. 7b). There was a nontriangular symmetry and linear slopes, consolidating the good pseudocapacitive behavior. The capacitance within the voltage region mainly resulted from the reduction of Fe3+ species to Fe2+ and the presence of oxygen vacancies for charge compensation (Qin et al. 2011). The capacitance values of two electrodes at various current densities were calculated based on their corresponding GCD curves and are plotted in Fig. 7c. The specific capacitance values were 72.2, 54.0, 41.5, 36.3, 33.0, 30.0, and 26.7 F g−1 at the current densities of 1, 2, 3, 5, 10, 15, and 20 A g−1, respectively. These excellent performances could be attributed to the nanoflakes and high specific surface areas which facilitated fast ion transfer by enhancing redox faradic reactions. This indicates that about 37 % of capacitance still remained as the current density increased from 1 to 20 A g−1, suggesting the superb rate capability. Figure 7d shows the cycling stability of the as-prepared BFO nanoflake-type electrodes by conducting charge/discharge tests at a current density of 5 A g−1 for 1500 cycles. The specific capacitance of the BFO electrode maintained 82.8 % of its initial value, indicating a good stability. The charge–discharge curves of the final 10 cycles are shown in the inset of Fig. 7d, showing almost the same symmetric shape, which implies that the BFO electrode remain unchanged for significant structural change during the charge/discharge processes.

The EIS measurement of the BFO electrode obtained after air annealing at 600 °C is presented in Fig. 7e. Capacitance can be interpreted as a measure for electrode activity, surface coverage, and the state-of-charge of an energy storage. The frequency response of capacitance reflects the amount of the surface area accessible to the electrolyte. Capacitance at high-frequency region shows the outer surface, which may depend on grain boundaries and other interparticle phenomena. Capacitance at low frequencies highlights the inner surface, which is primarily determined by the pore-size distribution and the speed of ion transport through the porous electrode (Qin et al. 2011). The plot at the high-frequency side was parallel to the X-axis whereas the subsequent regions were inclined to the X-axis suggesting that the charge transfer resistance rates at high-frequency regions was faster than those at low-frequency regions which could be due to an inherent property of ferrites.


In this study, we have demonstrated a simple and economical electrodeposition process to synthesize bismuth ferrite (BFO) for supercapacitor application. By changing the electrodeposition composition/condition, structure and morphology were greatly altered. Effects of annealing on BFO electrodes for 400, 500, and 600 °C were studied for evaluation of phase and surface morphology, if there is any. The cyclic voltammetry parameters of BFO electrodes were significantly enhanced in NaOH electrolytes than in other aqueous electrolytes. The maximum specific capacitance was obtained in 2 M NaOH electrolyte; therefore the same electrode was employed in the rest of the measurements. At 600 °C, BFO electrodes were superhydrophilic in nature, with the lower contact angle being beneficial for achieving enhanced specific capacitance. The effect of scan rate on supercapacitive properties of annealed BFO thin-film electrode was reported. The maximum specific capacitance of electrode annealed at 600 °C using galvanostatic charge–discharge curve was found to be 72.2 F g−1 at 1 A g−1 in 2 M NaOH electrolyte.



The authors wish to thank the Department of Science and Technology (DST), New Delhi, India, and the NRF, South Korea for selecting them in Indo-Korean Research Internship (IKRI) project to carry out the research for 12 months in Pusan National University, Busan, South Korea. Authors, R. S. Mane and M. Naushad, extend their gratitude to the Visiting Professor (VP) Unit of King Saud University (KSU) for the financial support.


  1. Adachi N, Denysenkov VP, Khartsev SI, Grishin AM (2000) Epitaxial Bi3Fe5O12 (001) films grown by pulsed laser deposition and reactive ion beam sputtering techniques. J Appl Phys 88:2734CrossRefGoogle Scholar
  2. Athoue L, Moser F, Dugas R, Crosnier O, Belanger D, Brousse T (2008) Variation of the MnO2 birnessite structure upon charge/discharge in an electrochemical supercapacitor electrode in aqueous Na2SO4 electrolyte. J Phys Chem C 112:7270CrossRefGoogle Scholar
  3. Bernardo MS, Jardiel T, Peiteado M, Caballero AC, Villegas M (2011) Reaction pathways in the solid state synthesis of multiferroic BiFeO3. J Europ Ceram Soc 31:3047CrossRefGoogle Scholar
  4. Biasotto G, Simoes AZ, Foschini CR, Zaghete MA, Varela JA, Longo E (2011) Microwave-hydrothermal synthesis of perovskite bismuth ferrite nanoparticles. Mater Res Bull 46:2543CrossRefGoogle Scholar
  5. Brezesinski T, Wang J, Polleux J, Dunn B, Tolbert SH (2009) Templated nanocrystal-based porous TiO2 films for next-generation electrochemical capacitors. J Am Chem Soc 131(5):1802CrossRefGoogle Scholar
  6. Chen C, Cheng J, Yu S, Che L, Meng Z (2006) Hydrothermal synthesis of perovskite bismuth ferrite crystallites. J Cryst Growth 291:135CrossRefGoogle Scholar
  7. Chen Z, Augustyn V, Jia X, Xiao Q, Dunn B, Lu Y (2012) High-performance sodium-ion pseudocapacitors based on hierarchically porous nanowire composites. ACS Nano 6:4319CrossRefGoogle Scholar
  8. Cheong SW, Mostovoy M (2007) Multiferroics: a magnetic twist for ferroelectricity. Nat Mater 6:13CrossRefGoogle Scholar
  9. Chu S, Majumdar A (2012) Opportunities and challenges for a sustainable energy future. Nature 488:294CrossRefGoogle Scholar
  10. Conway BE, Pell WG (2002) Power limitations of supercapacitor operation associated with resistance and capacitance distribution in porous electrode devices. J Power Sources 105:169CrossRefGoogle Scholar
  11. Das R, Khan GG, Varma S, Mukherjee GD, Mandal K (2013) Effect of quantum confinement on optical and magnetic properties of Pr-Cr-Codoped bismuth ferrite nanowires. J Phys Chem C 117(39):20209CrossRefGoogle Scholar
  12. David A, Tompsett C, Parker CS, Islam MS (2014) Rutile (β-) MnO2 surfaces and vacancy formation for high electrochemical and catalytic performance. J Am Chem Soc 136(4):1418CrossRefGoogle Scholar
  13. Dutta N, Bandyopadhyay SK, Rana S, Sen P, Himanshu AK (2013) Remarkably high value of capacitance in BiFeO3 Nanorod, Cornell University Library. arXiv 1309:5690Google Scholar
  14. Gao F, Yuan Y, Wing KF, Chen XY, Chen F, Liu JM, Ren ZF (2006) Preparation and photoabsorption characterization of BiFeO3 nanowires. Appl Phys Lett 89:102506CrossRefGoogle Scholar
  15. Gujar TP, Shinde VR, Kulkarni SS, Pathan HM, Lokhande CD (2006) Room temperature electrodeposition and characterization of bismuth ferric oxide (BFO) thin films from aqueous nitrate bath. App Surf Sci 252:3585CrossRefGoogle Scholar
  16. Jadhav VV, Patil SA, Shinde DV, Waghmare SD, Zate MK, Mane RS, Han SH (2013) Hematite nanostructures: morphology-mediated liquefied petroleum gas sensors. Sens Actuators B Chem. 188:669CrossRefGoogle Scholar
  17. Jaiswal A, Das R, Maity T, Vivekanand K, Adyanthaya S, Poddar P (2010) Temperature- dependent raman and dielectric spectroscopy of BiFeO3 nanoparticles: signatures of spin-phonon and magnetoelectric coupling. J Phys Chem C 114(29):12432CrossRefGoogle Scholar
  18. Kang J, Hirata A, Kang L, Zhang X, Hou Y, Chen L, Li C, Fujita T, Akagi K, Chen M (2013) Self-grown oxy-hydroxide@ nanoporous metal electrode for high-performance supercapacitors. Angew Chemie 52:1664CrossRefGoogle Scholar
  19. Kumar MM, Palkar VR, Srinivas K, Suryanarayana SV (2000) Ferroelectricity in a pure BiFeO3 ceramic. Appl Phys Lett 76:1CrossRefGoogle Scholar
  20. Kuo HY (2013) Effective property of multiferroic fibrous composites with imperfect interfaces. Smart Mater Struct 22:105005CrossRefGoogle Scholar
  21. Lang X, Hirata A, Fujita T, Chen M (2011) Nanoporous metal/oxide hybrid electrodes for electrochemical supercapacitors. Nat Nanotechnol 6:232CrossRefGoogle Scholar
  22. Liang Y, Schwab MG, Zhi L, Mugnaioli E, Kolb U, Feng X, Mullen K (2010) Direct access to metal or metal oxide nanocrystals integrated with one-dimensional nanoporous carbons for electrochemical energy storage. J Am Chem Soc 132(42):15030CrossRefGoogle Scholar
  23. Liu M, Gan L, Xiong W, Xu Z, Zhu D, Chen L (2014) Development of MnO2/porous carbon microspheres with a partially graphitic structure for high performance supercapacitor electrodes. J Mater Chem A 2:2555CrossRefGoogle Scholar
  24. Lokhande CD, Gujar TP, Shinde VR, Mane RS, Han SH (2007) Electrochemical supercapacitor application of pervoskite thin films. Electrochem Comm 9:1805CrossRefGoogle Scholar
  25. Luo Y, Kong D, Luo J, Wang Y, Zhang D, Qiu K, Cheng C, Ming C, Ting Li (2014) Seed-assisted synthesis of Co3O4@α-Fe2O3 core–shell nanoneedle arrays for lithium-ion battery anode with high capacity. RSC Adv. 4:13241CrossRefGoogle Scholar
  26. Mane RS, Lokhande CD, Todkar VV, Chung H, Yoon MY, Han SH (2007) Photosensitization of nanocrystalline TiO2 film electrode with cadmium sulphoselenide. Appl Surf Sci 253:3922CrossRefGoogle Scholar
  27. Martin LW (2010) Engineering functionality in the multiferroic BiFeO3 controlling chemistry to enable advanced applications. Dalton Trans 39:10813CrossRefGoogle Scholar
  28. Mo Y, Antonio MR, Scherson DA (2000) In situ Ru K-edge X-Ray absorption fine structure studies of electroprecipitated ruthenium dioxide films with relevance to supercapacitor applications. J Phys Chem B 104:9777CrossRefGoogle Scholar
  29. Mohan S, Subramanian B (2013) Nanostructured Bi(1−x)Gd(x)FeO3 a multiferroic photocatalyst on its sunlight driven photocatalytic activity. RSC Adv. 3:23737CrossRefGoogle Scholar
  30. Niesen TP, De Guire MR (2001) Review: deposition of ceramic thin films at low temperatures from aqueous solutions. J Electroceram 6:169CrossRefGoogle Scholar
  31. Palkar VR, Pinto R (2002) BiFeO3 thin films: novel effects. Pramana J Phys. 58:1003CrossRefGoogle Scholar
  32. Perejon A, Sanchez-Jimenez PE, Criado Jose M, Perez-Maqueda LA (2014) Thermal stability of multiferroic BiFeO3: kinetic nature of the β-γ transition and peritectic decomposition. J Phys Chem C 118(45):26387CrossRefGoogle Scholar
  33. Petzold J (2003) Applications of nanocrystalline softmagnetic materials for modern electronic devices. Scripta Mater 48:895CrossRefGoogle Scholar
  34. Qin H, Zhang H, Zhang BP, Xu L (2011) Hydrothermal synthesis of perovskite BiFeO3- BaTiO3 crystallites. J Am Ceram Soc 94(11):3671CrossRefGoogle Scholar
  35. Sartale SD, Lokhande CD, Giersig M, Ganesan V (2004) Novel electrochemical process for the deposition of nanocrystalline NiFe2O4 thin films. J Phys Condens Matter 16:773CrossRefGoogle Scholar
  36. Sathiya M, Prakash AS, Ramesha K, Tarascon JM, Shukla AK (2011) V2O5-anchored carbon nanotubes for enhanced electrochemical energy storage. J Am Chem Soc 133:16291CrossRefGoogle Scholar
  37. Schileo G (2013) Recent developments in ceramic multiferroic composites based on core/shell and other heterostructures obtained by sol-gel routes. Prog Solid State Chem 41:87CrossRefGoogle Scholar
  38. Singh VR, Dixit A, Garg A, Agrawal DC (2008) Effect of heat treatment on the structure and properties of chemical solution processed multiferroic BiFeO3 thin films. Appl Phys A 90:197CrossRefGoogle Scholar
  39. Subramanian V, Hall SC, Smith PH, Rambabu B (2004) Mesoporous anhydrous RuO2 as a supercapacitor electrode material. Solid State Ionics 175:511CrossRefGoogle Scholar
  40. Sun R, Nakajima A, Fujishima A, Watanabe T, Hashimoto K (2001) Photoinduced surface wettability conversion of ZnO and TiO2 thin films. J Phys Chem B 105:1984CrossRefGoogle Scholar
  41. Waghmare SD, Jadhav VV, Gore SK, Yoon SJ, Ambade SB, Lokhande BJ, Mane RS, Han SH (2012) Efficient gas sensitivity in mixed bismuth ferrite micro (cubes) and nano (plates) structures. Mater Res Bull 47:4169CrossRefGoogle Scholar
  42. Wang YP, Zhou L, Zhang MF, Chen XY, Liu JM, Liu ZG (2004) Room-temperature saturated ferroelectric polarization in BiFeO3 ceramics synthesized by rapid liquid phase sintering. Appl Phys Lett 84:1731CrossRefGoogle Scholar
  43. Wang G, Zhang L, Zhang J (2012) A review of electrode materials for electrochemical supercapacitors. Chem Soc Rev 41:797CrossRefGoogle Scholar
  44. Wang L, Ji H, Wang S, Kong L, Jiang X, Yang G (2013) Preparation of Fe3O4 with high specific surface area and improved capacitance as a supercapacitor. Nanoscale 5:3793CrossRefGoogle Scholar
  45. Winter M, Brodd RJ (2004) What are batteries, fuel cells, and supercapacitors? Chem Rev. 104:4245CrossRefGoogle Scholar
  46. Xia X, Zhang Y, Chao D, Guan C, Zhang Y, Li L, Ge X, Bacho IM, Tu J, Fan HJ (2014) Solution synthesis of metal oxides for electrochemical energy storage applications. Nanoscale 6:5008CrossRefGoogle Scholar
  47. Xie SH, Li JY, Proksch R, Liu YM, Zhou YC, Liu YY, Pan LN, Qiao Y (2008) Nanocrystalline multiferroic BiFeO3 ultrafine fibers by sol-gel based electrospinning. Appl Phys Lett 93:222904CrossRefGoogle Scholar
  48. Yan J, Khoo E, Sumboja A, Lee PS (2010) Facile coating of manganese oxide on tin oxide nanowires with high-performance capacitive behavior. ACS Nano 4:4247CrossRefGoogle Scholar
  49. Yoshimura M, Suchanek WL, Byrappa K (2000) Soft solution processing: a strategy for one- step processing of advanced inorganic materials. Mater Res Soc Bull 25:17CrossRefGoogle Scholar
  50. Yu L, Zhang L, Bin Wu H, Wen Lou X (2014) Formation of NixCo3− xS4 hollow nanoprisms with enhanced pseudocapacitive properties, Angew. Chemie 126:3785Google Scholar
  51. Zhai Y, Dou Y, Zhao D, Fulvio PF, Mayes RT, Dai S (2011) Carbon materials for chemical capacitive energy storage. Adv Mater 23:4828CrossRefGoogle Scholar
  52. Zheng H, Liu X, Diao C, Gu Y, Zhang W (2012) A separation mechanism of photogenerated charges and magnetic properties for BiFeO3 microspheres synthesized by a facile hydrothermal method. Phys Chem Chem Phys 14:8376CrossRefGoogle Scholar

Copyright information

© The Author(s) 2015

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (, 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 and Affiliations

  • Vijaykumar V. Jadhav
    • 1
    • 2
    • 4
  • Manohar K. Zate
    • 1
  • Shude Liu
    • 4
  • Mu. Naushad
    • 3
  • Rajaram S. Mane
    • 1
    • 2
    Email author
  • K. N. Hui
    • 4
    Email author
  • Sung-Hwan Han
    • 2
  1. 1.Center for Nanomaterials and Energy Devices, School of Physical SciencesSwami Ramanand Teerth Marathwada UniversityNandedIndia
  2. 2.Inorganic Nanomaterials Laboratory, Department of ChemistryHanyang UniversitySeoulRepublic of Korea
  3. 3.Advanced Materials Research Chair, Department of Chemistry, College of ScienceKing Saud UniversityRiyadhSaudi Arabia
  4. 4.School of Materials Science and EngineeringPusan National UniversityBusanKorea

Personalised recommendations