Processing math: 100%
J. Semicond. > 2015, Volume 36 > Issue 6 > 063001

SEMICONDUCTOR MATERIALS

Sub-stoichiometric functionally graded titania fibres for water-splitting applications

Vaia Adamaki1, A. Sergejevs2, C. Clarke2, F. Clemens3, F. Marken4 and C. R. Bowen1

+ Author Affiliations

 Corresponding author: Vaia Adamaki, Email: v.adamaki@bath.ac.uk

DOI: 10.1088/1674-4926/36/6/063001

PDF

Abstract: The photo-electro-chemical (PEC) splitting of water requires semiconductor materials with a minimum energy gap of 1.23 eV along with conduction and valence bands overlapping the oxidation of H2O and reduction of H+ respectively. The aim of this work is to overcome the limitations of stoichiometric titania by manufacturing fine scale fibres that exhibit a compositional gradient of oxygen vacancies across the fibre length. In such a fibre configuration the fibre end that is chemically reduced to a relatively small extent performs as the photoanode and the oxygen vacancies enhance the absorption of light. The fibre end that is reduced the most consists of Magnéli phases and exhibits metallic electrical conductivity that enhances the electron-hole separation. The structure and composition of the functionally graded fibres, which were manufactured through extrusion, pressureless sintering and carbo-thermal reduction, are studied using XRD and electron microscopy. Electrochemical impedance spectroscopy measurements were performed in a three-electrode electrochemical system and showed that the oxygen vacancies in the functionally graded fibres affect the flat band potential and have increased carrier density. The efficiency of the system was evaluated with PEC measurements that shows higher efficiency for the functionally graded fibres compared to homogeneous TiO2 or Magnéli phase fibres. The functionally graded and fine scale fibres have the potential to be used as an array of active fibres for water splitting applications.

Key words: titaniasuboxideswater splittingphotocurrent

Titania (TiO2) has been extensively investigated as an n-type semiconductor performing as a photo-anode for photo-electro-chemical (PEC) water splitting due to its chemical resistance,environmental suitability and low cost. Another main advantage of TiO2 is the suitable band edge positions,since a semiconductor for water splitting needs to have a minimum energy gap of 1.23 eV along with conduction and valence bands overlapping the oxidation of H2O and reduction of H+ respectively. The main limitations of stoichiometric TiO2 are its large band gap (3.2 eV) and high electron-hole recombination due to the short life of the excited electron. A variety of TiO2 structures have been investigated,for example carbon-doped TiO2[1] or Sr-doped TiO2[2],hydrogen treated TiO2[3],TiO2 nanostructures[3, 4, 5] and TiO2 heterostructures[2, 6] in order to overcome the limitations and achieve improved performance for water-splitting applications.

Previous work on Ti-suboxides has shown that it is possible to control the number oxygen vacancies and its electrical conductivity from 109 S/m (TiO2) to 104 S/m (Magnli phases)[7]. In this paper,we investigate the photo-electro-chemical properties of a novel functionally graded structure,whereby fine scale fibres are formed with a gradually increasing density of oxygen vacancies along its length. Figure 1 shows a schematic representation of a functionally graded fibre structure with one end consisting of TiO2 with oxygen vacancies introduced by carbo-thermal reduction and the other edge is chemically reduced to a larger extent and therefore consists primarily of Magnli phases (TinO2n1,3 < n < 10). The heavily reduced,and electrically conductive,end is then bonded with Ag wires using Al paste; which has been shown to form anohmic electrical contact with the Magnli phase region[7]. The photocurrent density efficiency was determined and the semiconductor-electrolyte interface was studied.

Figure  1.  (a) Schematic representation of the composite structure of a single fibre showing the gradient oxygen vacancies across the length of the fibre,and (b) image of a functionally graded fibre.

The TiO2 fibres were produced using a thermoplastic extrusion process. Titanium dioxide powder (PI-KEM,99.5%,0.3 μm particle size,specific surface area 7.49 m2/g) was pre-coated with three monolayers of stearic acid (93661,FlukaChemie AG,Switzerland). The stearic acid was solved in toluene and mixed with the ceramic powder in a jar mill with zirconia milling media for 12 h. The toluene was dried out using a rotary evaporator (Rotavapor R-134,B\"{u}chiLabortechnik AG,Switzerland). The pre-mixed powder was blended with polyethylene binder (1700MN18C Lacqtene PEBD,Arkema Group,Cedex,France) using a torque rheometer (HAAKE PolyLab Mixer,Rheomix 600,Thermo Scientific,Karlsruhe,Germany). For the two step mixing a temperature of 150 C (1st step) and 120 C (2nd step) was used. After mixing a thermoplastic homogeneous feedstock with 54 vol.% of TiO2 powder was achieved. This feedstock was used for thermoplastic extrusion of fibres with a diameter of 500 μm using a capillary rheometer (RH7-2,Malvern,Herrenberg,Germany) at a temperature of 120 C. A special ceramic die design (Empa,Switzerland) with an orifice of 500 μm was used to produce the fibres. The fibres were extruded with a ram speed of 0.5~mm/s and a pressure of 13 MPa[8]. The `green' TiO2 fibres were cut on a conveyor belt into 170 mm long lengths. The `green-body' fibres were then sintered at 1300 C for 1.5 h in chamber furnace (UAF,LENTON,UK) with a dwell stage at 500 C in order to burn out the binder. This sintering pattern was selected after optimization in order to achieve high density samples (> 97% of the theoretical) and avoid significant grain growth. After sintering,the diameter of the TiO2 fibres was 440 μm.

To produce the functionally graded fibres the TiO2 sintered fibres were reduced using a carbo-thermal process performed in a tubular furnace (LTF,LENTON,UK) with carbon black powder as reducing agent that was in contact with one end of the 10 mm long fibres. The reduction process was performed at 1300 C for 1 h under constant argon flow. The manufacturing and characterization of homogeneous TiO2 and Magnli phases fibres has been presented in detail in previous work[7] that was focusing on structural and electrical characterization. In the present work these homogenous fibres (length 10 mm,ϕ 0.44 mm) are also tested to compare with the functionally graded fibres. Figure 2 shows a schematic diagram of the process developed to manufacture the functionally graded titania fibres. To characterize the structure of the graded fibres and determine the phases present at both extremes of the fibre lengths,X-ray diffraction (XRD),Bruker D8-Advance using Cu-Kα wavelengths,and scanning electron microscopy (SEM,JEOL JSM6480LV) were used.

Figure  2.  Diagram of the manufacturing process of the functionally graded titania fibres.

The photocurrent of TiO2,Magnli phases and functional graded fibres was studied as a function of the intensity of the UV light using a novel LED reaction cell. The incident photon-to-photocurrent efficiency (IPCE) was determined according to the equation:

IPCE(%)=iphhcλPe×100,(1)
where iph is the photocurrent density,h is Planck's constant,c velocity of light,P the light power density,λ is the irradiation wavelength,and e is the elemental charge. PEC measurements on individual fibres were performed in a three electrode electrochemical system using a saturated calomel electrode (SCE) reference electrode and a platinum wire as a counter electrode in 1 M KOH electrolyte.

The reaction cell was equipped with an LED board with 36 LEDs controlled in 12 individual channels of three LEDs each ( Figure 3). The arrangement of LEDs was designed to provide an even illumination within the reaction cell. The LED board is an insulated metal substrate (IMS) printed circuit board (PCB) for better thermal management and each LED generates 800~mW of optical power at full electric power; this corresponds to 1.9 kW/m2 of optical power at a distance of 100 mm from the LEDs. In this work,tests were conducted on single fibres using 40% of the power,i.e. at 760 W/m2. There is a ±10% variation in optical power between LEDs,as well as ±2 nm variation in dominant wavelength[9]. In order to achieve an improved control of the optical power delivered to the fibres,an electrically erasable programmable read-only memory (EEPROM) chip was applied to the LED light source. The EEPROM holds the information about the intensity of each channel at different electrical power levels and the information on dominant wavelength offset from the desired wavelength; in this case 368 nm. Using this information the controller can adjust the input power to all channels to provide the correct optical power. Since the LEDs are heat sensitive,a temperature sensor was placed on the PCB of the UV light source and the sensor was used as an overheating protection. The LEDs were controlled with a pulse width modulated (PWM) signal generated by the LED driver circuitry. These LEDs are therefore cycled between being fully on and fully off and the duty cycle of the PWM signal determines the average intensity. UV light of 368 nm was chosen since previous work on TiO2 has reported that doping or oxygen vacancies have the greatest affect in this wavelength region[10, 11, 12].

Figure  3.  (a) LEDs board and (b) reaction cell.

The reactor used was a glass container with double walls with a space between the reactor vessel walls for a coolant to keep the temperature of the fibre in the reactor at a stable temperature. Linear sweeps of potential were collected electrode using an Ivium Technologies potentiostat. The interface of the semiconductor and the electrolyte was also studied using a Solartron SI 1250 coupled with a SI 1286 dielectric interface.

For an n-type semiconductor electrode at open circuit,the Fermi level is typically higher than the redox potential of the electrolyte[13] and hence there is an upward bending of the band edges. At positive potentials the holes move towards the electrode-electrolyte interface and electrons move to the interior of the semiconductor,where the Magnli phases are highly conductive and prevent electron-hole recombination. The gradual increase of the conductivity across the length of fibres improves the interconnectivity and the collection of the photo generated electrons at the base of the fibres[14]. At a certain potential the Fermi level is at the same energy level as the solution redox potential and therefore there is no band bending. This potential is referred to as the flat band potential (Efb) which can be calculated based on the Mott-Schottky relationship by measuring the apparent capacitance as a function of the applied potential (Equation (2)). The donor density can be calculated from the gradient (n) of the (1/C2 versus E) curve and Efb determined by extrapolation to the condition,C = 0.

1C2=2(EEfbkT/e)NDεε0eA2,(2)
ND=2εε0A2en,(3)
where ND is the carrier density,k the Boltzmann constant,T the temperature,ε the dielectric constant of the anodic film,ε0 the permittivity of free space,e the charge of an electron,and A the electrode surface. There are two capacitance values to be considered,the space charge region and the double layer. Since the space charge capacitance is much smaller than the double layer capacitance[15] the contribution of the space charge capacitance to the total capacitance is considered negligible. The equivalent circuit used for the modelling of the electrochemical impedance spectroscopy measurements is an R (R-C) circuit[16].

The morphology and structure of the functionally graded fibres were characterized by SEM and XRD. Figures 4(a) and 4(b) present SEM images of lightly reduced TiO2x fibre end (i.e. furthest away from carbon source) and Figures 4(c) and 4(d) show the heavily reduced Magnli phase end of the functionally graded fibre.

Figure  4.  SEM images of (a),(b) the TiO2x end of functionally graded fibres and (c),(d) the Magnli phases end of the functionally fibres.

Using the linear intercept method,the measured grain size was smaller at the TiO2x end of the functionally graded fibre. The grain sizes are 5.9 and 8.3 μm for the TiO2x and the Magnli phases end respectively. At the Magnli phase end of the fibres oxygen diffusion is more intense and this can lead to grain boundary migration that increases the grain size[17]. After sintering and reduction the diameter is 440 μm across the whole length of the fibres. XRD spectra for the functionally graded fibres are presented in Figure 5 and show the different phases formed at each end of the fibres. The XRD spectrum of the TiO2x fibre end shows the presence of rutile TiO2 and titanium suboxides while the XRD spectrum of the Magnli phase fibre end shows the presence of titanium suboxides whereas the TiO2 peaks are no longer present.

Figure  5.  XRD spectra of the opposite end of the composite fibre. (a) TiO2x end and (b) Magnli phases end.

To investigate the effect of the oxygen vacancies on the electrode-electrolyte interface electrochemical impedance measurements on single Magnli phases and functionally graded fibres were also conducted. Measurements conducted on single TiO2 fibres were subject to noise due to their low electrical conductivity (109 S/m) and accurate fitting of the impedance measurements was therefore not possible. Figures 6(a) and 6(b) show the Mott-Schottky plots for the Magnli phase and functionally graded fibres. Both curves exhibit positive slopes suggesting the n-type semiconductor behaviour of both materials.

Figure  6.  Mott-Schottky plots for (a) Magnli phases single fibre and (b) functionally graded single fibre.

The flat band potential was determined to be 1.92 V versus SCE for the Magnli phase fibre whereas for the functionally graded fibre it was -2.33 V versus SCE. The Mangli phases exhibit 2-D electronic conductivity and therefore the number of available carries is not as high in this region compared to the TiO2x fibre end where the oxygen vacancies introduced by partial reduction increase the carrier density. By determining the gradient (n) of the Mott-Schottky plots in Figure 6 and using Equation (3) the carrier density was determined; for the homogenous Magnli phase fibre the carrier density is 4.16 × 1014 cm3 and for the functionally graded fibre is 5.72 × 1017 cm3. Oxygen vacancies are known to be shallow donors for the rutile phase of TiO2 and therefore increase the carrier density[18]. In the case of the Magnli phases the structure and the conduction mechanism changes and thus the oxygen vacancies do not increase the carrier density[19]. The EIS measurements ( Figure 6) that showed the better performance (more negative flat band potential) of the functionally graded fibres are confirmed from the photocurrent measurements that are shown in Figures 7(a)-7(c) which compare the photocurrent densities of measurements of TiO2,Magnli phase and functionally graded fibres. The photocurrent density produced from the functionally graded fibre is much higher (0.786 mA/cm2) than both the TiO2 (0.032 mA/cm2) and Magnli (0.065 mA/cm2). The IPCE was also calculated as shown in Table 1 at 0.241 V versus SCE (0 V versus RHE). The TiO2 fibre has the lowest efficiency,where the Magnli phases fibre has an increased performance but is not as high as the functionally graded fibre,which is in agreement with the measured carrier density. In addition to the higher carrier density the functionally graded fibres have improved interconnectivity due to the gradually increasing oxygen vacancies that enhance the electron-hole separation.

Figure  7.  Photocurrent versus potential (versus SCE) under UV light of (a) TiO2 fibre,(b) Magnli phases fibre,and (c) composite fibre (760 W/m2,368 nm).
Table  1.  The incident photon-to-photocurrent efficiency (IPCE) of TiO2,Magnli phases and the functionally graded fibres (TiO2x-Magnli phases).
DownLoad: CSV  | Show Table

The calculated IPCE for the functionally graded fibres at 368 nm is higher than the efficiency reported in other work on modified TiO2[1, 5, 11] and therefore shows the promise of functionally graded fibres as part of a fibre array for water splitting applications. Further work on the graded fibres will explore the measurement of the photocurrent under visible light,the determination of the efficiency and testing of larger scale fibre arrays.

This paper has investigated work to enhance the performance of TiO2 as a photo anode for water splitting by forming functionally graded and fine scale fibres that could be used as an array of active fibres. The fibres have been formed by carbo-thermal reduction on extruded TiO2 fibres and the low-cost extrusion process is of interest to readily form large scale arrays of such structures. XRD shows that the fibre end furthest from the carbon source during the reduction process consists mostly of rutile TiO2 along with titanium suboxides (TiO2x) due the oxygen vacancies introduced by carbo-thermal reduction. This fibre end is placed in contact with the electrolyte and acts to absorb the UV light. The fibre end that is heavily reduced and in direct contact with the carbon source during the reduction process consists of Magnli phases that exhibit electrical conductivity close to metallic (104 S/m). This end of fibre is used to encourage electron-hole separation. As shown from the EIS data,the level of oxygen vacancies along the fibre length affect the flat band potential that moves to negative values (at both ends) and are therefore more beneficial of water splitting applications. In addition,the TiO2x fibre end increases the carrier density due to the increased shallow donors. The photocurrent density of the functionally graded fibres was significantly higher compared to homogeneous TiO2 and Magnli phases fibres reaching an efficiency of 34.8% and demonstrates the potential of functionally graded fine scale TiO2 fibres for water splitting applications.

Acknowledgements

The research leading to the materials development and characterisation was from the European Union's Seventh Framework Programme (FP7/2007-2013)/ERC Grant Agreement no. 320963 on Novel Energy Materials,Engineering,Science and Integrated Systems (NEMESIS). Reactor development was supported by The European Union under FP7 Project 309846,"Photocatalytic Materials for the Destruction of Recalcitrant Organic Industrial Waste - PCATDES.''



[1]
[2]
[3]
[4]
[5]
[6]
[7]
[8]
[9]
[10]
[11]
[12]
[13]
[14]
[15]
[16]
[17]
[18]
[19]
Fig. 1.  (a) Schematic representation of the composite structure of a single fibre showing the gradient oxygen vacancies across the length of the fibre,and (b) image of a functionally graded fibre.

Fig. 2.  Diagram of the manufacturing process of the functionally graded titania fibres.

Fig. 3.  (a) LEDs board and (b) reaction cell.

Fig. 4.  SEM images of (a),(b) the TiO2x end of functionally graded fibres and (c),(d) the Magnli phases end of the functionally fibres.

Fig. 5.  XRD spectra of the opposite end of the composite fibre. (a) TiO2x end and (b) Magnli phases end.

Fig. 6.  Mott-Schottky plots for (a) Magnli phases single fibre and (b) functionally graded single fibre.

Fig. 7.  Photocurrent versus potential (versus SCE) under UV light of (a) TiO2 fibre,(b) Magnli phases fibre,and (c) composite fibre (760 W/m2,368 nm).

DownLoad: CSV
DownLoad: CSV
DownLoad: CSV

Table 1.   The incident photon-to-photocurrent efficiency (IPCE) of TiO2,Magnli phases and the functionally graded fibres (TiO2x-Magnli phases).

DownLoad: CSV
[1]
[2]
[3]
[4]
[5]
[6]
[7]
[8]
[9]
[10]
[11]
[12]
[13]
[14]
[15]
[16]
[17]
[18]
[19]
1

Demonstration of irradiation-resistant 4H-SiC based photoelectrochemical water splitting

Yan Pei, Wenhao Geng, Lingbo Xu, Can Cui, Xiaodong Pi, et al.

Journal of Semiconductors, 2024, 45(11): 112503. doi: 10.1088/1674-4926/24050011

2

State-of-the-art advances in vacancy defect engineering of graphitic carbon nitride for solar water splitting

Jie Li, Kaige Huang, Yanbin Huang, Yumin Ye, Marcin Ziółek, et al.

Journal of Semiconductors, 2023, 44(8): 081701. doi: 10.1088/1674-4926/44/8/081701

3

Recent progress on nanostructured bimetallic electrocatalysts for water splitting and electroreduction of carbon dioxide

Can Cui, Xiaosong Hu, Liaoyong Wen

Journal of Semiconductors, 2020, 41(9): 091705. doi: 10.1088/1674-4926/41/9/091705

4

Engineering the photoelectrochemical behaviors of ZnO for efficient solar water splitting

Mengmeng Ma, Yanbin Huang, Jun Liu, Kong Liu, Zhijie Wang, et al.

Journal of Semiconductors, 2020, 41(9): 091702. doi: 10.1088/1674-4926/41/9/091702

5

Precision photonic integration for future large-scale photonic integrated circuits

Xiangfei Chen

Journal of Semiconductors, 2019, 40(5): 050301. doi: 10.1088/1674-4926/40/5/050301

6

Studies of Water V. Five Phonons in Protonic Semiconductor Lattice Model of Pure Liquid Water

Binbin Jie, Chihtang Sah

Journal of Semiconductors, 2017, 38(7): 071001. doi: 10.1088/1674-4926/38/7/071001

7

Photodeposited FeOOH vs electrodeposited Co-Pi to enhance nanoporous BiVO4 for photoelectrochemical water splitting

Aihua Jia, Miao Kan, Jinping Jia, Yixin Zhao

Journal of Semiconductors, 2017, 38(5): 053004. doi: 10.1088/1674-4926/38/5/053004

8

Effect of ultrasound on reverse leakage current of silicon Schottky barrier structure

O.Ya Olikh, K.V. Voitenko, R.M. Burbelo, JaM. Olikh

Journal of Semiconductors, 2016, 37(12): 122002. doi: 10.1088/1674-4926/37/12/122002

9

Design of current mirror integration ROIC for snapshot mode operation

Hari Shanker Gupta, A S Kiran Kumar, M. Shojaei Baghini, Subhananda Chakrabarti, Sanjeev Mehta, et al.

Journal of Semiconductors, 2016, 37(10): 105001. doi: 10.1088/1674-4926/37/10/105001

10

Progress in complementary metal-oxide-semiconductor silicon photonics and optoelectronic integrated circuits

Hongda Chen, Zan Zhang, Beiju Huang, Luhong Mao, Zanyun Zhang, et al.

Journal of Semiconductors, 2015, 36(12): 121001. doi: 10.1088/1674-4926/36/12/121001

11

Solid State Physics View of Liquid State Chemistry Ⅲ. Electrical Conductance of Pure and Impure Water

Binbin Jie, Chihtang Sah

Journal of Semiconductors, 2014, 35(4): 041001. doi: 10.1088/1674-4926/35/4/041001

12

Solid State Physics View of Liquid State Chemistry Ⅱ. Electrical Capacitance of Pure and Impure Water

Binbin Jie, Chihtang Sah

Journal of Semiconductors, 2014, 35(2): 021001. doi: 10.1088/1674-4926/35/2/021001

13

Solid State Physics View of Liquid State Chemistry——Electrical conduction in pure water

Binbin Jie, Chihtang Sah

Journal of Semiconductors, 2013, 34(12): 121001. doi: 10.1088/1674-4926/34/12/121001

14

Avalanche-enhanced photocurrents in pin silicon waveguides at 1550 nm wavelength

Yong Zhao, Chao Xu, Xiaoqing Jiang, Huiliang Ge

Journal of Semiconductors, 2013, 34(6): 064009. doi: 10.1088/1674-4926/34/6/064009

15

Photoconductive properties of organic-inorganic Ag/p-CuPc/n-GaAs/Ag cell

Khasan Sanginovich Karimov, Muhammad Tariq Saeed, Fazal Ahmad Khalid, Zioda Mirzoevna Karieva

Journal of Semiconductors, 2011, 32(7): 072001. doi: 10.1088/1674-4926/32/7/072001

16

Accurate surface potential determination in Schottky diodes by the use of a correlated current and capacitance voltage measurements. Application to n-InP

Ali Ahaitouf, Abdelaziz Ahaitouf, Jean Paul Salvestrini, Hussein Srour

Journal of Semiconductors, 2011, 32(10): 104002. doi: 10.1088/1674-4926/32/10/104002

17

Photolithography Process Simulation for Integrated Circuitsand Microelectromechanical System Fabrication

Zhou Zaifa, Huang Qing'an, Li Weihua

Chinese Journal of Semiconductors , 2006, 27(4): 705-711.

18

Temperature Dependence of Vacuum Rabi Splitting in a Single Quantum Dot-Semiconductor Microcavity

Zhu Kadi, Li Waisang

Chinese Journal of Semiconductors , 2006, 27(3): 489-493.

19

High-Integrated-Photosensitivity Negative-Electron-Affinity GaAs Photocathodes with Multilayer Be-Doping Structures

Wang Xiaofeng, Zeng Yiping, Wang Baoqiang, Zhu Zhanping, Du Xiaoqing, et al.

Chinese Journal of Semiconductors , 2005, 26(9): 1692-1698.

20

Sensitivity of Total-Dose Radiation Hardness of SIMOX Buried Oxides to Doses of Nitrogen Implantation into Buried Oxides

Zheng Zhongshan, Liu Zhongli, Zhang Guoqiang, Li Ning, Li Guohua, et al.

Chinese Journal of Semiconductors , 2005, 26(5): 862-866.

1. Gong, H., Wang, L., Zhou, K. et al. Improved photocatalytic performance of gradient reduced TiO2 ceramics with aligned pore channels. 2022, 1(3): 100025. doi:10.1016/j.apmate.2021.11.011
2. Pylnev, M., Chang, W.-H., Wong, M.-S. Shell of black titania prepared by sputtering TiO 2 target in H 2  + Ar plasma. Applied Surface Science, 2018. doi:10.1016/j.apsusc.2018.08.103
  • Search

    Advanced Search >>

    GET CITATION

    Vaia Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. Journal of Semiconductors, 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001
    V Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. J. Semicond., 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001.
    shu

    Export: BibTex EndNote

    Article Metrics

    Article views: 2507 Times PDF downloads: 14 Times Cited by: 2 Times

    History

    Received: 02 February 2015 Revised: Online: Published: 01 June 2015

    Catalog

      Email This Article

      User name:
      Email:*请输入正确邮箱
      Code:*验证码错误
      Vaia Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. Journal of Semiconductors, 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001 ****V Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. J. Semicond., 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001.
      Citation:
      Vaia Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. Journal of Semiconductors, 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001 ****
      V Adamaki, A. Sergejevs, C. Clarke, F. Clemens, F. Marken, C. R. Bowen. Sub-stoichiometric functionally graded titania fibres for water-splitting applications[J]. J. Semicond., 2015, 36(6): 063001. doi: 10.1088/1674-4926/36/6/063001.

      Sub-stoichiometric functionally graded titania fibres for water-splitting applications

      DOI: 10.1088/1674-4926/36/6/063001
      More Information
      • Corresponding author: Email: v.adamaki@bath.ac.uk
      • Received Date: 2015-02-02
      • Accepted Date: 2015-03-18
      • Published Date: 2015-01-25

      Catalog

        /

        DownLoad:  Full-Size Img  PowerPoint
        Return
        Return