plasmon-induced water splitting under visible light ......instructions for use title plasmon-induced...
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Instructions for use
Title Plasmon-Induced Water Splitting under Visible Light Irradiation using Gold Nanostructured Strontium Titanate SingleCrystal Substrate
Author(s) 鐘, 玉磬
Citation 北海道大学. 博士(情報科学) 甲第11973号
Issue Date 2015-09-25
DOI 10.14943/doctoral.k11973
Doc URL http://hdl.handle.net/2115/59961
Type theses (doctoral)
File Information Yuqing_Zhong.pdf
Hokkaido University Collection of Scholarly and Academic Papers : HUSCAP
Plasmon-Induced Water Splitting under Visible Light Irradiation
using Gold Nanostructured Strontium Titanate Single Crystal
Substrate
Thesis by
Yuqing Zhong
In Partial Fulfillment of the Requirements
for the Degree of
Doctor of Philosophy
RESEARCH INSTITUTE FOR ELECTRONIC SCIENCE
HOKKAIDO UNIVERSITY
SAPPORO, JAPAN
2015
Dedication
DEDICATED
TO
MY PAPERENTS
i
Table of Contents
Acknowledgements .............................................................................................................. iv
Thesis Abstract ..................................................................................................................... vi
Chapter 1 .............................................................................................................................. 1
Introduction .......................................................................................................................... 1
1.1 Background and Motivation .................................................................................... 1
1.2 Origin of Photoelectrochemical (PEC) Water Splitting .......................................... 4
1.3 PEC Water Splitting over Semiconductor Photocatalysts ....................................... 8
1.3.1 Basic Principles of PEC Water Splitting ....................................................... 8
1.3.2 Common Materials for PEC Water Splitting ............................................... 11
1.3.3 Development of Visible Light Driven Water Splitting ................................ 15
1.3.4 Plasmon-enhanced Water Splitting .............................................................. 20
1.4 Evaluation of PEC Water Splitting ........................................................................ 24
1.4.1 Stoichiometry of H2 and O2 Evolution ........................................................ 24
1.4.2 Time Course of H2 and O2 Evolution .......................................................... 24
1.4.3 Turnover Number ........................................................................................ 24
1.4.4 Quantum Yield ............................................................................................. 26
1.4.5 Photoresponse .............................................................................................. 27
1.5 Current Scenario and Challenges .......................................................................... 28
1.6 Aim and outline of this thesis ................................................................................ 30
1.7 References ............................................................................................................. 31
Chapter 2 ............................................................................................................................ 44
Plasmon-Induced Water Splitting Using Two Sides of the Same SrTiO3 Single-Crystal
Substrate ............................................................................................................................. 44
2.1 Abstract .................................................................................................................. 44
2.2 Introduction ........................................................................................................... 45
ii
2.3 Experimental details .............................................................................................. 47
2.3.1 Niobium doped strontium titanate single crystals ....................................... 47
2.3.2 Preparation of Au-NPs on a SrTiO3 substrate ............................................. 50
2.3.3 Construction of the water splitting device ................................................... 51
2.3.4 Quantitative determination of hydrogen evolution ..................................... 53
2.3.5 Quantitative determination of oxygen evolution ......................................... 54
2.4 Results and discussion ........................................................................................... 57
2.4.1 Characterization of Au-NPs ......................................................................... 57
2.4.2 Numerical simulations of Au-NPs on SrTiO3.............................................. 60
2.4.3 Influence of irradiation wavelength on H2 and O2 generation .................... 62
2.4.4 Influence of pH value combinations on H2 and O2 generation ................... 64
2.4.5 Mechanism for the plasmon-assisted water splitting reaction ..................... 67
2.4.6 Stability of the plasmon-assisted water splitting system ............................. 70
2.5 Conclusions ........................................................................................................... 71
2.6 References ............................................................................................................. 72
Chapter 3 ............................................................................................................................ 76
Co-catalyst Effects on Hydrogen Evolution in the Plasmon-Induced Water Splitting
System ................................................................................................................................ 76
3.1 Abstract .................................................................................................................. 76
3.2 Introduction ........................................................................................................... 78
3.3 Experimental details .............................................................................................. 82
3.3.1 Preparation of noble metal and metal oxide co-catalyst .............................. 82
3.3.2 Electrochemical measurements ................................................................... 82
3.4 Results and discussion ........................................................................................... 84
3.4.1 Elimination of the Schottky barrier effect ................................................... 84
3.4.2 Characteristics of the Ru and Rh species thin film on Pt board .................. 89
3.4.3 Water splitting performance using various H2 evolution co-catalyst .......... 93
3.4.4 Dependence of co-catalyst thickness on water splitting activity ................. 98
iii
3.5 Conclusions ......................................................................................................... 100
3.6 References ........................................................................................................... 101
Chapter 4 .......................................................................................................................... 104
Plasmon-Induced Water Splitting Utilizing Heterojunction Synergistic Effect between
SrTiO3 and Rutile TiO2 ..................................................................................................... 104
4.1 Abstract ................................................................................................................ 104
4.2 Introduction ......................................................................................................... 105
4.3 Experimental details ............................................................................................ 107
4.3.1 Preparation and characterization of the TiO2 thin film .............................. 107
4.4 Results and discussion ......................................................................................... 109
4.4.1 Dependence of Pt co-catalyst thickness on water splitting activity .......... 109
4.4.2 Characteristics of the TiO2 thin film .......................................................... 113
4.4.3 Water splitting performance by TiO2 with different crystalline phases ..... 115
4.5 Conclusions ......................................................................................................... 118
4.6 References ........................................................................................................... 119
Chapter 5 .......................................................................................................................... 122
Summary and Future Perspectives ................................................................................... 122
5.1 Summary ............................................................................................................. 122
5.2 Future Perspectives .............................................................................................. 124
List of Publications ........................................................................................................... 126
iv
Acknowledgements
First and foremost, I would like to express my special appreciation and thanks to my
supervisor, Prof. Hiroaki Misawa, he has been a tremendous mentor for me. I would like
to thank him for encouraging my research and for allowing me to grow as a research
scientist. His advice on both research as well as on my career have been priceless. I am
also deeply grateful for the continuous support, insight and patience of Prof. Kosei Ueno.
He is a good teacher who encouraged and expected us to think more independently about
our experiments and results. I would also like to thank Prof. Tomoya Oshikiri for his
scientific advice and many insightful discussions and suggestions. Thanks to their careful
and friendly supervision, ideas and comments I could learn a lot in these years. Without
their constant trust and, sometimes, gentle prodding, this thesis would not have been
completed. I will forever be thankful to my former college research advisor, Prof. Hongbo
Sun. He has been helpful in providing advice many times during my graduate school
career. I still think fondly of my time as an undergraduate student in his lab. His
recommendation played a vital role in my application for the doctoral program in
Hokkaido University. He was the reason why I decided to go to pursue a career in
scientific research. His enthusiasm and love for research is contagious.
I would like to give special thanks to Ms. Yumiko Yamaguchi, Ms. Yukiko Sugawara
and Ms. Rumiko Kobayashi, who helped me with many application procedures. I am also
very grateful to Ms. Yuko Mori, who offered the constant practical help which is essential
for the smooth running of any project. She kindly assisted me with my experiment and
offered her invaluable expertise on technical skills to me. The improvement of my
Japanese was also attributed to the interesting discussion with her. The Research Institute
for Electronic Science has been a wonderful community in which to grow up as a research
student, the personal and professional relationships forged in these years will stay with me
forever. Sincere thanks go to Dr. Xu Shi, who generously introduced me to the
v
mechanisms of photochemistry and also helped me to solve problems in the experiments
when I first came to this laboratory. The discussion with him was meaningful and
enjoyable. Special thanks also go to Mr. Han Yu, who helped me in study and life. We had
so much memorable experience in Japan together.
I would also like to express my deep gratitude to other laboratory members, Dr. Quan
Sun, Dr. Hiyori Uehara, Dr. Jie Li, Dr. Youzhuan Zhang, Dr. Yu Teng, Dr. Olivier Lecarme,
Ms. Narisu, Mr. Jingchun Guo, Mr. Xiaolong Yang, Mr. Ahamed Shalan, Mr. Takaya
Tokiwa, Mr. Sho Nozawa, Mr. Keisuke Nakamura, Mr. Daisuke Aoyo, Mr. Hidenori Asahi,
Mr. Masamitsu Muto, Mr. Yuki Kotake, Mr. Yuki Matsuzuka and Mr. Yoshiomi Kamata.
We’ve all been there for one another and have taught ourselves and each other many tools
and issues of experimental method. I know that I could always ask them for advice and
opinions on lab related issues. They are wonderful and generous colleagues and partners.
It has been a pleasure working with you. I appreciate help of Mr. Ko Onishi and Ms.
Naomi Kawai from the research support department for facilities maintenance and their
meticulous guidance. I would also like to thank all of my friends who supported me and
incented me to strive towards my goal.
I am indebted to the China Scholarship Council (CSC) for their generous funding,
which removed financial concerns from my decision to embark on this journey.
As a final note, I owe special thanks to my family. Words cannot express how
grateful I am to my parents for all of the sacrifices that they have made for me. I dedicate
this thesis to them.
vi
Thesis Abstract
As a potential solution to the energy crisis, H2 production from water via solar
irradiation has attracted global attention over the last few decades, because the chemical
energy in H2 can be stored for long periods. Numerous attempts have been made since the
photoelectrochemical (PEC) water splitting based on an n-type TiO2 photoanode was
discovered. However, because of the wide band gap of the semiconductor materials
adopted, only UV light can be used to directly drive the water splitting reaction. The UV
irradiation merely accounts for 5% of the solar spectrum. Visible and infrared light, which
take the major part, are still underutilized. Therefore, it is of significance to extend the
light-energy conversion to longer wavelengths, especially to the visible and infrared
regions. Common materials used for water splitting are particulate. They are undesired
because extra energy is required to separate H2 and O2, which evolved in the same reaction
chamber. In addition, an external electric bias is necessary in PEC water splitting. To
overcome these problems, a plasmon-induced water splitting system under visible light
irradiation using gold nanostructured strontium titanate (SrTiO3) single crystal is presented
in this study. Gold nanoparticles (Au-NPs) with particle size of several tens of nanometer
were employed for SrTiO3 surface decoration, which enhanced the SrTiO3 photorespons in
visible wavelength region due to the localized surface plasmon resonance. It is proposed
that the simultaneous evolution of H2 and O2 can be realized without an electric wire
connecting the anode and the cathode and with space conserved for light irradiation on the
anode side through the use of two sides of the same semiconductor substrate.
In order to fabricate Au-NPs, a 3-nm Au thin film was sputtered on SrTiO3 surface
and annealed in nitrogen atmosphere at 800°C. After annealing, the gold films
transformed to a discontinuous nanoparticle structure. The Au-NPs exhibited
characteristic plasmon resonance band with a peak at ca. 630 nm. Numerical simulation
shows that the electromagnetic field intensity is greatly enhanced around the interface
between gold and SrTiO3 substrate. The stoichiometric evolution of H2 and O2 was clearly
vii
demonstrated. The efficiency action spectrum closely corresponds to the plasmon
resonance spectrum, indicating that the plasmon-induced charge separation at the
Au/SrTiO3 interface promotes water oxidation and the subsequent reduction of a proton on
the backside of the SrTiO3 substrate. The photo energy derived from visible light
irradiation is successfully converted to chemical energy, which is stored as the form of H2
gas. As a substitution of the conventional external electric bias, the chemical bias used to
promote water splitting is significantly reduced to 0.23 V by plasmonic effects (Chapter
2).
The co-catalyst effect on hydrogen evolution in the plasmon-induced water splitting
is discussed in detail. A Pt board was stick on the SrTiO3 substrate via In-Ga alloy to
obtain ohmic contact. The water spitting yield with this SrTiO3/Pt composite substrate was
remarkably enhanced. Subsequently, the Pt board was decorated with a noble metal or
metal oxide as a co-catalyst for H2 evolution. Enhanced evolution of H2 and O2 with
stoichiometric ratio was demonstrated with all kinds of co-catalysts. Rhodium thin layer
exhibited relatively high performance as a 3-fold increment compared with the absence of
any co-catalyst. The separate evolution of H2 and O2 was successfully realized, so as to
suppress the undesirable reverse reactions of water splitting. A rational evaluation method
of the co-catalyst is thus developed based on the elimination Schottky barrier (Chapter 3).
A facile plasmon-enhanced water splitting system using gold nanostructured
semiconductor heterojunction is described. With a larger potential gradient in the energy
band, the electron transfer can be facilitated by using semiconductors with different band
positions. The substrate composed of single crystal SrTiO3 with the rutile TiO2 thin film
heterojunction exhibited enhanced water spitting activity compared with the absence of
TiO2 thin film because the back electron transfer reaction might be prevented due to the
synergistic effect. The effect on the H2 evolution efficiency of the thickness of the Pt
co-catalyst film was also explored (Chapter 4).
Herein, the plasmon-enhanced water splitting was demonstrated in visible
wavelength with gold nanoparticles loaded SrTiO3. The H2 and O2 generation efficiency is
viii
highly dependent on the pH values of the solution environments. It is expected that the
plasmon resonant wavelength of Au nanostructures can be tuned by simply changing their
shape and/or size to cover a large part of the solar spectrum. It indicates the possibility of
constructing an artificial photosynthesis system with low energy consumption. The results
of these studies warrant future research to evaluate the mechanism of plasmon-enhanced
water splitting and provide a facility approach for further design of the plasmon-enhanced
solar energy conversion devices.
Keywords: electrochemistry, artificial photosynthesis, strontium titanate (SrTiO3),
localized surface plasmons, photochemistry, water splitting, nanostructures.
1
Chapter 1
Introduction
1.1 Background and Motivation
The dramatic increase of the world population in the last century raises the question of
how long the resources of our planet will last. The world population has been estimated to
be 7.209 billion by December 6th, 2014 and it is expected to increase even more rapidly
according to the World Population Report of the United Nations Population Fund.[1]
At the same time the world energy consumption, mostly based on fossil fuels such as
oil, coal and gas is also increasing.[2]
These resources are created by a very slow
geological process and their quantity is therefore limited. As a finite resource, it is
reasonable to be expected to reach a limitation and decline in the production afterwards.
The oil and natural gas have been predicted to last for a number of decades by several
estimations, while the coal could last up to a few hundred years, although there is no
agreement on the exact numbers. Most of these analyses are based on conventional oil
storage, but the numbers will be different if new oil resources can be found and extracted.
Currently, oil companies are investing in unconventional oil, extracted it with techniques
different from the traditional oil well method and from places that can not be reached with
the present technology. This oil is definitely more expensive than the conventional one.
The world economy will be seriously damaged if the production of oil starts to decrease
rapidly. Therefore an effective solution of this problem by means of the introduction of
new technologies must be activated well ahead of schedule since the time scale for
introducing new technologies to our society could be very long.
The use of fossil fuels is also relevant to a number of other issues. For instance, when
fossil fuels are consumed and burnt, CO2 is emitted into the atmosphere. This gas will
remain in the atmosphere for many years because it can not be fixed by nature rapidly. The
2
carbon cycle will be broken consequently. Human activities have been confirmed to give
rise to the increase of the CO2 concentration in the atmosphere. The CO2 is supposed to
bring about some environmental problems because it is a green house gas. The average
temperature in the globe will be increased along with the CO2 amount in the atmosphere.
The warming of our planet will probably result in the melting of the arctic ice and glaciers
and finally changes of climate with negative influence of all the life forms. Actually, the
global temperature has already been observed increasing recently. The solution for the
decrease of the CO2 production needs to be mastered as quickly as possible.[3]
Figure 1.1 Total World Energy Consumption by Source 2013
So far, there has been some CO2 sequestration method proposed by several
researchers. However, these solutions all involve capturing and trapping the emitted CO2
underground. Therefore, they are not feasible solutions for long term since they cannot
close the carbon cycle, but merely a postponement of the situation as a result.
When we pursuit a civilized society with the energy sources that are especially
sustainable and renewable to substitute the fossil fuels, the solution has eventually been
the sun that always seen shining in the sky over our heads. As a yellow dwarf star, the sun
has a diameter of about 109 times compared with the one of the earth. The nuclear fusion
of hydrogen into helium takes place in the sun and thus produces energy. This kind of
energy diffuses into the surrounding outer space as the form of kinetic energy of light
radiation or particles after generated in the core of the sun. It can be considered as a source
3
of energy that will never exhaust on human time scale, because the sun is supposed to
keep shining for billions more years.
In Figure 1.2, the solar irradiance is plotted as a function of wavelength for standard
condition (air mass 1.5, i.e., AM 1.5). The average flux of solar irradiation reaching the
earth surface is 174.7 W/m2 taking the scattering and absorption by the atmosphere and
the clouds into consideration. The tremendous potential of the solar energy is obvious
because the human average power consumption worldwide is about 15 TW every year. If
we could build a photoelectric conversion device with a solar energy conversion efficiency
of 10%, only 0.2% of the earth surface area needs to be covered with such kind of devices
in order to obtain the energy of 15 TW as mentioned.
Nevertheless, the solar irradiation is not a source of energy that is constantly available.
Because the day and night alters and it also highly dependent on the weather conditions,
such as sunny and cloudy day, etc. Hence, this kind of energy has to be stored as a readily
useable form. Whereas for the purpose of making large amount of energy stored,
electricity has never been an ideal choice. Superior performance could be obtained by
chemical energy with a higher energy density. In such scenario, the energy is stored in
chemical bonds and could be released whenever necessary by a simple chemical reaction,
combustion in the case of fossil fuels for instance.
Figure 1.2 The radiation energy in solar spectrum as a function of wavelength.
4
1.2 Origin of Photoelectrochemical (PEC) Water Splitting
Innovations in both science and technology are inspired by the increasing demand for
renewable energy. Being considered as one of the most potential clean energy carriers,
hydrogen possesses the unique characters. It has a very high energy density. The enthalpy
of combustion is 286 kJ/mol. And since the only product after the burning of hydrogen is
water, without any other pollutant or green house gas, it is environmental friendly.
Furthermore, hydrogen also has some important industrial applications, e.g., fuel cell
industry and industrial ammonia synthesis. Up until now, the production of hydrogen is
mainly by means of biomass or fossil fuels reforming reactions.[4]
The commercial
hydrogen gas is produced by the steam reforming of natural gas (methane) in industry.
CH4 + 2H2O 4H2 + CO2 ΔG0
= 131 kJ mol-1
(1-1)
If we take energy and environmental issues into consideration, the present technique
is defective and even unacceptable. Firstly, very high temperature (700-1000°C) is
necessary during this process since it is an intensive endothermic reaction. Secondly, this
reaction has to consume the non-renewable fossil fuels and there is green house gas CO2
emission as a byproduct in the process. These drawbacks during the industrial production
process hinder the extensive application of H2. As a consequence, the production of H2 via
environmental-friendly and renewable methods has been come an urgent issue.
Water is a perfect source of hydrogen from the view point of saving fossil fuels and to
avoid the undesired CO2 emissions. However, external energy driving force, e.g.,
electrical power, is needed in order to split water into H2 and O2. The process is a general
knowledge as the electrolysis of water.
H2O(g) 1/2O2(g) + H2(g) ΔH0 = 241.8 kJ mol
-1 (1-2)
An inexpensive and clean energy substitution that is capable to supply the power for
our planet could be expected as the form of H2 if we can make use of a renewable source,
such as solar energy, as the energy input.[5]
Some hydrogen production methods from
5
water using solar light have been proposed. One of them is electrolysis of water by a solar
cell. Besides, promising strategies have also been provided through photocatalytic or (PEC)
water splitting to achieve this purpose.[6-8]
Honda and Fujishima demonstrated the photoelectrochemical water splitting for the
first time under ultraviolet (UV) irradiation using n-type single-crystal TiO2
photoe1ectrode in 1972.[9, 10]
Under UV irradiation, electrons and holes are generated in TiO2, as shown in Figure
1.3. With some external electric bias, water can be reduced by the photo-induced electrons
to generate H2 on the Pt counter electrode. On the other hand, O2 will be formed on the
TiO2 photoelectrode via the water oxidation by the remained holes. During this reaction
course, the UV light harvesting and the electron generation for water reduction are
through the agency of the TiO2 semiconductor. It plays a key role in the conversion of the
irradiation energy into the chemical energy, which is stored in H2, by splitting the water
molecules. This kind of functional semiconductor is thus commonly referred to as
photocatalyst in this research field. In the last few decades, a great deal of research on the
photocatalytic water splitting based on the semiconductor materials have been proceed
after the pioneer work of Honda and Fujishima.
Figure 1.3 The sketch map of Honda-Fujishima effect-water splitting using a TiO2
photoelectrode.
6
Among the various kinds of semiconductors, only a few of them are capable of
performing the photocatalytic water splitting reaction. As is known to all, there is a band
gap separating the conduction band (CB) and the valance band (VB) in semiconductors.
The electrons can be excited from CB to VB and leaving holes in the VB if the
semiconductor is irradiated by an incident light with the energy larger than its band gap.
Then H2 and O2 will be subsequently formed through the water reduction by the electrons
and the water oxidation by the holes respectively to complete the overall water splitting.
Theoretically, in order to ensure the water splitting reactions to carry out normally,
there are three key issues. For the thermodynamically aware, the electrons and holes
generated by the incident light excitation should have the appropriate redox potentials so
as to perform the reduction and the oxidation reactions of the water molecules. In other
words, the bottom position of the conduction band needs to be more negative than the
redox potential of H+/H2 (0 V vs. NHE), and meanwhile the top position of the valence
band needs to be more positive than the redox potential of O2/H2O (1.23 V vs. NHE), as
shown in Figure 1.4. As a consequence, only the semiconductors with a band gap larger
than 1.23 eV and with proper positions of CB and VB are candidates for water splitting.
Figure 1.4 Fundamental steps for water splitting reaction by solid-state photocatalysts.
Based on the above mentioned analysis, it seems that the ideal options of the materials
for water splitting are semiconductors with relatively large band gaps. To date, a lot of
7
such semiconductors have been investigated for PEC water splitting, such as TiO2,[11]
ZrO2,[12]
K4Nb6O17 [13, 14]
et al. Nevertheless, a severe drawback of the large band gap
semiconductors is that they can only absorb the UV light. Whereas taking the efficiency
issue into consideration, the energy composition of the solar spectrum (AM 1.5) is
constituted by ca. 2% ultraviolet light, 47% visible light (corresponding to the wavelength
region from 380 nm to 780 nm) and 51% infrared light. A major part of the solar energy
will thus be wasted if we use the large band gap semiconductors for water splitting.
Therefore, many new types of photocatalysts that respond to visible light are currently
under investigation. Besides these basic requirements and efficiency problems, the
stability of the semiconductor materials in aqueous solutions under irradiation of light is
another important issue. Due to their appropriate energy band positions, several
chalcogenide semiconductors have been considered as suitable photocatalysts for water
splitting that respond to visible light irradiation. Even though some of these chalcogenide
semiconductors, CdS for example,[15, 16]
is capable of splitting water very efficiently under
visible light irradiation,[17]
the CdS itself will also be oxidized by the photogenerated holes
during the water splitting reaction process. A dramatic decrease of the water splitting
efficiency is inevitable as the result of the decomposition of the catalytic material CdS.
Therefore, for most chalcogenide photocatalysts, this is a critical defect. At present, a
great challenge still remains for the development of semiconductors materials that are
stable and feasible for photoelectrochemically splitting water very efficiently under the
solar irradiation.
8
1.3 PEC Water Splitting over Semiconductor Photocatalysts
1.3.1 Basic Principles of PEC Water Splitting
Only the deep ultraviolet light with a wavelength shorter than 190nm can be used to
split water directly, since the visible light cannot be absorbed.[18]
As mentioned in the
former section, at least 1.23 V bias is required to promote the electrolysis of water. The
bias voltage at this amount is corresponding to an irradiation light wavelength of about
1000 nm. Therefore, the utilization of the visible region of the solar spectrum for water
splitting could be expected theoretically, in condition that the irradiation is used very
effectively. The original work of H2 generation from water splitting was done by Honda
and Fujishima in 1970s. As shown in Figure 1.5, the typical PEC water splitting cell they
have used is composed of a photoanode of n type TiO2 semiconductor and a Pt counter
electrode.
Figure 1.5 Photoelectrochemical water splitting cell based on n type semiconductor
TiO2 photoelectrode.[19]
The surface region of the TiO2 photoelectrode is charged, as the result of the charge
transfer at the interface between the electrolyte and TiO2, since they contact. The charges
move from the TiO2 to the electrolyte, a surface charge area is thus formed and the energy
9
band of the TiO2 bends upwards, as depicted in the figure. The potential barrier resulted
by this energy band bending is referred to as Helmholtz barrier. The property of the
semiconductor and the characteristic of the aqueous electrolyte both affect this barrier. At
the interface between the electrolyte and semiconductor, this Helmholtz barrier could
drive the separation between electrons and holes. Furthermore, the transportation of
chargers at the bending band region would also be facilitated. Electron and hole pairs will
be generated in the TiO2 when it is irradiated by light with an energy lager than its
bandgap value. The electrons excited by light irradiation will transfer to the counter
electrode and generate H2 evolution by reducing water, whereas the holes will remain at
the TiO2 surface and generate O2 evolution via water oxidation.[20, 21]
The reactions on the
two electrodes can be described by equations as follow:
Photanode: H2O + 2h+ 2H
+ + 1/2O2 E
0ox = -1.23 V (1-3)
Cathode: 2H+ +2e
- H2 E
0red = 0 V (1-4)
In principle, to drive the solar water splitting, a minimum amount bias voltage of
1.23V is generally required between the two electrodes. The bandgap of the
semiconductors used in the water splitting reaction is usually larger than 1.23V
accordingly. Nevertheless, the essential conditions for a water splitting system to function
stably include but are not limited to a suitable bandgap value. An external electric bias is
necessary to drive the water splitting reaction in many situations, even using a
semiconductor with a bandgap larger than 1.23 eV, such as Fe2O3 and WO3. Actually, the
external bias needed is highly dependent on the energy band structure of the
semiconductors.
There are three major steps in a typical photocatalytic reaction, as shown in figure 1.6.
They all have strong impact on the photocatalytic capability of a photocatalyst.
10
Figure 1.6 Processes involved in photocatalytic overall water splitting on a heterogeneous
photocatalyst.
(i) Electron hole pairs generation in photocatalysts by means of photon absorption. If
the incident irradiation has an energy larger than that of the semiconductor bandgap, the
photons from the incident light can be absorbed and electron hole pairs will be generated
consequently. The electrons will transfer to the conduction band of the semiconductor
after the excitation by the incident photons. On the other hand, the holes will remain at the
valence band. The electrons and holes will reduce and oxidize water molecules to form H2
and O2 generation respectively to accomplish the overall water splitting.
(ii) The separation and migration of the electron hole pairs generated by
photoexcitation. Generally, before the electron hole pairs participate in the photocatalytic
reactions, they need to separate and transfer to the reaction sites on the photocatalysts
surface. During this process, the crystal structure, crystallinity and the particle size of the
semiconductor material show a great influence. Defects often function as a charge trap and
also a recombination center for the electrons and holes generated by photoexcitation.
Therefore, they are undesired in the semiconductor used as a photocatalytic material since
11
the activity will sure be ruined. The photocatalyst with relatively higher crystallinity takes
advantage for charge separation and migration in this respect since the number of defects
would be smaller. The photocatalyst particle size should be small in order to obtain higher
efficiency. The reason is that the surface area and the number of the reactive sites are
larger for smaller particles. Furthermore, the distance that an electron or a hole has to
transfer to the surface reaction sites is shorter so as to reduce the recombinations.
(iii) The chemical reactions on the semiconductor surface. This step is influenced by
the active sites and the area of the surface. A large part of the electrons and holes
generated in the above steps will be lost in the recombination instead of participate in the
water splitting, in spite of the fact that they possess enough potentials thermodynamically
for the reaction. To address this issue, many kinds of co-catalysts, such as Pt,[22]
Pd,[23]
Ru,[24]
NiO,[25]
RuO2,[26]
and Cr/Rh oxides,[27]
are decorated on the surface of
photocatalysts. The function of these co-catalysts is generally considered to be as the
active sites, where the photocatalytic reactions take place. Except for the formation of the
active sites on the semiconductor surface, increasing the surface area of photocatalysts, e.g.
fabrication of some nanostructures on the photocatalysts, is another effective method to
enhance the photocatalytic activity.
These three steps are all essential for photocatalytic water splitting reaction. Hence, an
ideal photocatalyst should possess suitable energy band structure, bulk properties and
surface characters. Until now, the photocatalytic water splitting research still remains in
the laboratory level. This means that some mechanisms are not yet clearly understood.
And visible light driven photocatalysts with acceptable efficiency have not been
developed. A lot of efforts have been made to explore new type of photocatalysts and to
functionalize or modify photocatalysts that already exist.
1.3.2 Common Materials for PEC Water Splitting
Some essential requirements have to be fulfilled in the semiconductor materials used
for the water splitting reaction so as to obtain a considerable efficiency. Generally, the
12
semiconductors should have conduction band and valence band straddling the redox
potentials of E0(H
+/H2) and E
0(O2/H2O).
[28] By this means, the water splitting reaction can
be promoted by the photogenerated electrons and holes with enough electrochemical
potential in the absence of any external bias. Moreover, the semiconductors should be
capable of absorbing solar irradiation efficiently and also stable for a long term during the
water splitting process. The absorption ability for solar irradiance is affected by the
semiconductor bandgap. It greatly influences the solar to hydrogen conversion efficiency.
The solar energy spectrum on the basis of irradiation energy and photon numbers is shown
in Figure 1.7. The UV irradiation only takes a quite small part of the whole solar spectrum
as can be seen in the figure.
Figure 1.7 Number of photons in solar spectrum, versus photon energy. The optical
band gaps of common metal oxide photocatalysts are indicated for comparison.[29]
The minimum bandgap for a semiconductor used in PEC water splitting is 1.23 eV in
theory. However, because of the energy loss in the PEC water splitting process, the
photons that could be utilized practically, usually have energy larger than 1.23 eV. And
the solar to hydrogen conversion efficiency is still much smaller than we expected. There
are several reasons that can induce this energy loss, such as the polarization within the
13
PEC, the recombination between electrons and holes, and the potential loss caused by the
resistance of electrodes and contact. The energy loss has been estimated to be about 0.8
eV. The practical energy limit of the photons feasible for PEC water splitting is thus
determined to be about 2.0 eV. The great effort that has been devoted into the research of
visible light respond PEC water splitting is also based on this concern.
Many researchers have focused on the investigation of new type semiconductor
materials with preferable performance for PEC water splitting ever since the innovative
work with a TiO2 photoelectrode succeeded. So far, numerous materials have been
developed for the PEC water splitting, including metal oxides such as TiO2,[30-42]
Fe2O3,
ZnO,[43-50]
Nb2O5, BiVO4,[51-64]
ZrO2, WO3,[65-72]
metal nitrides such as Ta3N5,[73-76]
metal
phosphides such as GaP,[77, 78]
metal titanate such as SrTiO3, BaTiO3, metal tantalate such
as KTaO3, and metal oxynitrides such as TaON[79-82]
. These materials are all used as
photoelectrodes. They can be classified as either photoanodes or photocathodes according
to the different reactions occur on their surfaces. As described in the former section, there
are three main steps in the PEC water splitting: solar irradiation absorption, charge
separation and migration, and surface chemical reactions.[83]
The intrinsic properties of the
catalytic materials, e.g. energy band structure, bandgap value, crystallinity, electronic
conductivity, and particle morphology, have a significant influence on these processes.
The energy band structures of typical catalytic semiconductor materials and their
corresponding bandgap values are shown in Figure 1.8.[84]
The normal hydrogen electrode
(NHE) at pH=0 and vacuum energy level are both employed. For metal oxides, only the
ones with bandgaps large enough, such as SrTiO3, ZrO2 and ZnO, can straddle the both
redox potentials of water. However, the light harvesting ability will be limited if the
bandgap is too large. And the PEC water splitting efficiency will also be seriously affected.
Whereas in the case of metal oxides with relatively small bandgap, such as WO3 and
Fe2O3, external bias is necessary to promote the water splitting reaction since the
conduction band position is not more negative than the reduction potential of water.
Furthermore, the Fe2O3 has a very poor electrical conductivity, the recombination between
14
electrons and holes is thus severe because of its limited carrier diffusion length. CdSe and
CdS seem to have both the suitable CB and VB positions and small bandgap values.
However, they are not stable during the water splitting process. They can be readily
oxidized to metal oxides and the ideal energy band structure would no longer exist.[85, 86]
Figure 1.8 The bandgap and band structure potentials of typical semiconductors relative
to the redox potential of water; the potentials are versus normal hydrogen electrode (NHE)
at pH=0 and vacuum potential.[84]
For metal nitrides and metal oxynitrides, in despite of that the band structure and
electronic property of catalytic materials can be modified by the incorporation of nitrogen,
the nitride materials will finally lose their activity upon the irradiation because of
photodecomposition. A considerable percentage of the solar irradiation can be absorbed
by silicon, because its bandgap is quite small (1.1 eV). However, silicon has a valence
band that is not more positive than the water oxidation potential. An external bias is thus
inevitable. It can be supplied by making hybrid devices, e.g., a hybrid system of PEC
device and dye sensitized solar cell.[87-90]
Nevertheless, because of the large surface
overpotentials and surface oxidation, silicon is also unstable under irradiation.[91]
The
solutions of the issues in catalytic semiconductors about light harvesting, energy band
structures, electronic property, and chemical durability, have been systematically
15
investigated. Some strategies have been proposed such as nanostructure decoration and
chemical modification, e.g., element doping, design of semiconductor surface
heterojunction, and co-catalyst modification.
1.3.3 Development of Visible Light Driven Water Splitting
With the purpose of water splitting in the absence of any external bias, semiconductor
materials with flat band potential more negative than the H+/H2 potential, such as SrTiO3
or KTaO3, are preferred. However, as shown in Figure 1.9, these materials are usually
unable to absorb visible light because of their large bandgaps.[92]
The solar energy
conversion efficiency is very low as a result.
Figure 1.9 Photoelectrolysis of water using a SrTiO3 photoanode. Due to the position of
conduction and valence band edges hydrogen and oxygen are evolved without need of
external bias.[93]
So far, visible light driven photocatalytic materials have been investigated extensively.
For UV respond metal oxide photocatalysts, as can be seen in Figure 1.8, the bottoms of
16
the conduction bands are slightly more negative than 0 V, whereas the tops of the valence
bands are more positive than 3 V (vs. NHE at pH 0). As a consequence, visible light can
not be absorbed due to the large bandgap. However, these metal oxide photocatalysts are
capable of oxidizing water since there is a considerable difference between the top of the
valence band and the oxidation potential of water (1.23 V vs. NHE). Hence, it would be
of significance if we can maintain the conduction band position and meanwhile improve
the band structure. Figure 1.10 shows the main techniques to utilize visible light by a
metal oxide with a large bandgap. They are summarized accordingly as follows.
Figure 1.10 Primary approaches of energy band engineering for a metal oxide to
obtain the visible light response.
(i) Doping with transition-metal ions. One of the most common used methods for the
crystal structure modification of a metal oxide is to dope it with some other elements. In
general, the dopant will substitute a lattice point of the crystalline host material.
Consequently, it forms a donor or acceptor level in the forbidden band of the
semiconductor by the dopant which is a transition-metal ion. These doping levels
functions as a visible absorption center. Unfortunately, the dopant usually serves as
discrete energy levels instead of an energy band. The efficient transfer of the electrons and
holes will be seriously affected as the result.[94]
Furthermore, when we dope the host metal
oxide with another element, the charge balance is destroyed in many circumstances.
17
Vacancies that function as recombination centers can be readily generated. Therefore, the
doping method is not an ideal solution for the metal oxide material used as visible light
driven photocatalyst to some extent.
(ii) Valence band control using the p orbitals of an anion or the s orbitals of metal ion.
In despite of some successful examples about the above mentioned doping method, the
adverse effect of the defects working as recombination centers is still serious. Moreover,
the discrete doping levels formed by the dopants hinder the carrier transfer. In contrast, it
would be preferable for the metal oxide to have a continuous valence band formed by
atomic orbitals of the constituent elements. A lot of researchers have reported this kind of
special photocatalysts with a valence band-control.[95]
Figure 1.11 Basic principle of visible light driven water splitting based on spectral
sensitization depicted by energy band alignment
(iii) Spectral sensitization. In the early 1970s, H. Gerischer demonstrated the spectral
sensitization of semiconductor particles with large bandgap.[96]
Since then, in order to
realize the H2 generation by visible light driven water splitting, a great effort has been
made to the development of this strategy.[97-104]
The main process of the spectral sensitized
water splitting is shown in Figure 1.11. Organic dyes and inorganic semiconductors with a
narrow bandgap can be employed as sensitizers. Their bandgap should be small enough to
18
absorb the visible light. In addition, their excited-state potential needs to be higher than
the conduction band of the metal oxide to facilitated electron injection. The electrons
injected are involved in the water reduction to generate H2 at a co-catalyst such as Pt.
While the sensitizers are compensate with electrons from donor molecules. Water is the
ultimate electron donor in a system without the sacrifice reagent. However, sacrificial
reagent such as alcohols, organic acids, and hydrocarbons, are commonly used to avoid
the side reactions such as H2-O2 recombination. In this situation, the electron transfer from
the sensitizer to co-catalyst, e.g. Pt, is mediated by the semiconductor. There is a
competition between the water reduction and the electron back transfer to the oxidized
sensitizer. Therefore, the H2 evolution activity is highly dependent on the semiconductor
material, the sensitizer and the co-catalyst in this system.[105-115]
To date, a number of
visible light driven photosynthesis systems have achieved apparent quantum efficiency as
high as several tens of percent for H2 generation from water using spectral sensitizers with
suitable electron donor.
Figure 1.12 Overview of water splitting on Z-scheme photocatalysis system with an
iodate (IO3-) and iodide (I
-) ion redox couple.
[28]
19
Another main approach for achieving visible light driven water splitting is to apply a
two-step photoexcitation process using two different photocatalysts, as depicted in Figure
1.12. This strategy is known as the Z-scheme water splitting.[116-124]
It was inspired by
natural photosynthesis through which the green plants convert solar energy into chemical
energy. In such a two-step system, the water splitting process is divided into two stages:
one for H2 generation and the other for O2 generation. A solution containing the shuttle
redox couple (Red/Ox in the figure) will connect them. At the H2 evolution photocatalyst,
H2 evolves via water reduction by the photoexcited electrons, while the holes in its
valence band oxidize the reductant (Red) to oxidant (Ox). The oxidant is subsequently
reduced back to the reductant by photoexcited electrons generated at the O2 evolution
photocatalyst, where the holes oxidize water to evolve O2. The energy requirement for
photocatalysis is substantially reduced by this system. The utilization of visible irradiance
for water splitting has thus become more efficient. This means that the semiconductor with
the capability of either reducing or oxidizing water can be used in overall water splitting.
For instance, some visible light active oxides such as SnO2 can be used as O2 evolution
photocatalysts in condition that they can reduce certain oxidant to a reductant. Similarly,
non-oxide photocatalysts such as sulfides, oxynitrides and dyes, can be used as H2
evolution photocatalysts in condition that they can oxidize certain reductant to an oxidant.
Therefore, many kinds of semiconductor materials can be utilized in the Z-scheme water
splitting despite that they are unqualified in one-step system. Furthermore, separate
evolution of H2 and O2 can be realized in Z-scheme system via a separator by which only
the redox mediators can be transferred. It is theoretically impossible to obtain separate
generation of H2 and O2 in a conventional one-step system because H2 and O2 are
simultaneously evolved at small semiconductor particles. However, there is a critical
drawback of the Z-scheme systems that the number of photons required in a two-step
photoexcitation system is twice that for a one-step system to achieve overall water
splitting.
20
1.3.4 Plasmon-enhanced Water Splitting
Plasmon is a collective oscillation of the free electron gas density in a conductive
material, as shown in Figure 1.13. Light below the plasma frequency will be reflected
since the electrons in the metal screen its electric field. Light above the plasma frequency
will be transmitted since the electrons respond too slowly to screen it. Surface plasmons
are coherent delocalized electron oscillations confined to the surfaces of conductive
materials. The interaction between surface plasmons and light is very strong. If the real
part of the dielectric function becomes zero, at the plasmon frequency, there will be a
resonance in the absorption. Intense electric fields can be generated on the surface of the
metal nanoparticles when they are irradiated by light at their plasmon frequency. The size,
shape and material of the nanoparticle and its distance from other nanoparticles all have
significant impact on the frequency of this resonance.[125-128]
For instance, if we fabricate
the silver nanoparticle to a size small enough, its plasmon resonance can be shifted from
the UV region into the visible range. Similarly, the regulation of the gold plasmon
resonance from the visible region to the infrared region is also possible via the
nanoparticle size miniaturization.
Figure 1.13 Schematic of plasmon oscillation for a sphere, showing the displacement of
the conduction electron charge cloud relative to the nuclei.[129]
Improved photocatalytic water splitting under visible irradiation has been
demonstrated by a number of researchers via plasmonic metal nanoparticles deposition on
the top of anatase TiO2. In such a scenario, the H2 and O2 generation is detected by gas
chromatography with mass spectrometry, and the photocurrents are monitored via a
21
potentiostat. Thomann et al. have observed the enhanced photocurrent of water splitting
using Au/Fe2O3 as the photocatalyst. The maximum enhancement was as high as 11-fold.
An interesting phenomenon was also discovered that the position of the gold nanoparticles
in the Fe2O3 film had a great impact on the photocurrent enhancement peak position and
curve shape.[130]
Enhanced photocatalytic water splitting was also reported by Torimoto et
al. using Au core-SiO2 shell particles decorated with CdS nanoparticles.[131]
As shown in
Figure 1.14, Liu et al. deposited Au nanoparticles on the top of catalytic TiO2 as
photoanode. They have demonstrated photocurrents through the water splitting reaction
with the enhancement of 5-fold and 66-fold at the visible irradiation wavelength of 532
nm and 633 nm, respectively.[132]
Figure 1.14 (a) Schematic diagram of the photoelectrochemical measurement setup. (b)
Photocurrent of anodic TiO2 with and without Au nanoparticles irradiated with λ = 633 nm
light for 22 s.[132]
Ingram et al. reported a visible light driven photocurrent using nitrogen-doped TiO2
decorated by Ag nanocubes with a 10-fold enhancement compared with in the absence of
Ag nanocubes.[133]
Duan et al. also observed enhancement of light absorption by Ag
nanoparticles on CdS with a SiO2 intermediate layer in between. This intermediate layer
can be used to regulate the plasmon resonance peak effectively.[134]
Some researchers have
focused on the investigation of the optimum weight percentage of Au nanoparticles in
TiO2 instead of their nanoparticle geometry.[135, 136]
However, the optimum Au weight
22
percentage distinguished from each other in the case of photocatalytic semiconductor with
different morphology. It can not lead to a profound comprehension of the physical
mechanism of the water splitting enhancement. Despite of the considerable enhancement
excited by the plasmon resonance, the overall solar to energy conversion efficiencies are
still quite low especially in the visible wavelength region.
Figure 1.15 Plasmon-assisted photocurrent generation and water oxidation from visible to
near-infrared wavelength using a Au-nanorods/TiO2 Electrode.[137]
Nishijima et al. reported the plasmon-enhanced photocurrent generation and water
oxidation by visible and near infrared light irradiation, as shown in Figure 1.15.[137-140]
They fabricated gold nanorods array on the surface of TiO2 photoelectrode. Stoichiometric
evolution of oxygen was demonstrated via water oxidation through the irradiation of this
photocurrent generation system. The electrons are supplied by water molecules, since
there is no electron donor except a potassium perchlorate aqueous solution, which was
employed as an electrolyte solution. The plasmonic optical antenna effect of the gold
nanorods promoted the stoichiometric evolution of oxygen and hydrogen peroxide via the
four- or two-electron oxidation process of water molecules, respectively. After the electron
transfer from gold to TiO2, it is speculated that the water oxidation recovered effectively
23
via the multiple holes generated by plasmon-induced charge excitation. This photoelectric
conversion system as proposed is considered to be a promising approach for artificial
photosynthesis using visible and near-infrared light.
24
1.4 Evaluation of PEC Water Splitting
To date, hundreds of materials have been investigated as photocatalytsts, and
thousands of corresponding applications have already been published in academic journals
concerning the modification and improvement of the existing photocatalysts so as to
enhance the photocatalytic activity. Thereupon, the evaluation of the capability of these
photocatalysts is necessary to be within a unified standard for both theoretical research
and practical application.
1.4.1 Stoichiometry of H2 and O2 Evolution
For a water splitting process without any sacrificial reagent employed, both H2 and O2
should be formed in a stoichiometric ratio, i.e., the amount of the H2 generation should be
twice that of the O2 generation. Occasionally, the H2 evolution can be observed while the
O2 evolution is undetectable. In this situation, the amount of H2 evolution is usually very
small even compared with the amount of the photocatalyst. It is thus not confirmed if such
kind of reaction is a photocatalytic process and it is crucial to clarify that this is not a
sacrificial reaction.
1.4.2 Time Course of H2 and O2 Evolution
In a typical water splitting reaction, the amounts of the H2 and O2 evolution should
increase with the irradiation time. The amount of evolved H2 and O2 over per unit
irradiation time is one of the most important indicators for the assessment of the
photocatalytic activity. The long term stability of a photocatalyst is usually investigated by
repeated experiments. After the water splitting reaction for a long time, there should be no
or negligible decrease in the activity for a stable photocatalyst.
1.4.3 Turnover Number
In the research field of catalysis, turnover number (TON) is an important index for the
25
character of many catalytic materials. In photocatalysis, TON is also indispensable to
evaluate a catalyst. The quantity of the H2 and O2 evolved should overwhelm that of the
photocatalysts employed. Otherwise, the process could be a chemical reaction instead of a
photocatalytic reaction. There still remains a possibility that the H2 and O2 evolution are
generated from the chemical reactions between water and semiconductor materials, or
from the self-decomposition of the semiconductors. None of these is an essentially
catalytic process.
In general, turnover number is defined as the number of reacted molecules per active
site.
TON = number of reacted molecule
number of active sites (1-5)
Nevertheless, precise determination of the number of active sites on a photocatalyst
surface is impossible in the case of heterogeneous photocatalysis. Hence, an alternative
method is proposed for practical application. The number of photocatalyst molecules is
employed in above equation instead of the number of active sites. The equation is thus
modified as follows:
TON = number of reacted electrons
number of molecules in a photocatalyt (1-6)
The number of reacted electrons can be calculated from the number of molecules of
H2 or O2 gas evolution. Since the number of all the photocatalyst molecules is definitely
larger than that of the active sites on a certain photocatalyst surface, the TON value
calculated by the above equation is actually smaller than the real value. Sometimes the
photocatalytic activity is normalized by the weight of the photocatalyst employed, e.g.,
mmol h-1
g-1
. However, that is somewhat inaccurate since the photocatalytic activity tends
to be saturated with the weight of photocatalyst if the amount of photocatalyst used is
large enough for a certain experimental condition. The optimum quantity of certain
photocatalyst needs to be determined for each experimental system individually. In this
situation, the photocatalytic activity mainly depends on the photon absorption by the
26
photocatalyst unless the irradiation is too strong.
1.4.4 Quantum Yield
Since photocatalytic water splitting has become a worldwide concern, numerous
photocatalysts have been investigated using different experimental apparatus with distinct
parameters by different laboratories. Even for the same photocatalysts, the activities will
show a considerable difference, such as the evolution time course of H2 or O2 derived
from the measurements, if they are measured with different experimental setups or in
different conditions. Therefore, such kinds of activities are unacceptable for comparison in
order to evaluate the efficiencies of the photocatalysts.
At present, quantum yield is generally acknowledged as a standard for the evaluation
of the efficiencies of various photocatalysts reported by different research groups. The
definition of the quantum yield is depicted as the follow equation:
Quantum yield = number of reacted electrons
number of absorbed photons (1-7)
The influence of different light sources can be excluded by using this quantum yield
value for the assessment. However, the number of photons absorbed by the photocatalysts
is very difficult to measure in practical terms. Therefore, the evaluation of the
performance of photocatalysts is commonly indicated with an extended term “external
quantum yield” or “apparent quantum yield”, abbreviated to EQY or AQY respectively.[19]
AQY % = number of reacted electrons
number of incident photons x 100 (1-8)
Spectroradiometer can be used for the measurement of the number of incident photons.
Due to the light reflection and scattering of the solid semiconductors, the number of
absorbed photons is definitely smaller than that of incident photons. Therefore, the AQY
is usually lower than the real quantum yield.
It should be noted that the quantum yield discussed above is different from the solar
energy conversion efficiency which is frequently used in the assessment of solar cells.
27
Solar energy conversion % = Output energy as H2
Energy of incident solar light x 100 (1-9)
Since the activities of most photocatalysts are too low to measure, there is only a few
photocatalysts exhibiting passable solar energy conversion efficiency until now. However,
for the end of solar hydrogen production, the photocatalytic water splitting should finally
be evaluated in terms of the solar energy conversion efficiency.
1.4.5 Photoresponse
When a photocatalyst is irradiated by light with energy larger than its band gap, water
splitting should occur. The action spectrum is very important for the investigation of the
photoresponse, particularly for a photocatalyst that responds to visible light. During the
measurement of the action spectrum, monochromatic light is generally obtained using
band-path and interference filters. Even if a material is capable for visible light absorption,
it does not always have the photocatalytic activity induced by the excitation of the visible
light absorption. The onset wavelength can be determined when using cut-off filters to
observe the photoresponse. In dark condition with constant stirring, water splitting on
some metal oxides can proceed by mechanocatalysis instead of photocatalysis.[141, 142]
Therefore, for the purpose of confirming the photocatalytic reaction and excluding the
possibility of the mechanocatalytic water splitting, some control experiments such as in
the absence of any photocatalyst or any irradiation should be performed.
28
1.5 Current Scenario and Challenges
Photocatalytic water splitting offers an attractive potential solution for the
production of environmentally clean energy carriers obtained from renewable material
sources and abundant solar energy.[143, 144]
The design and synthesis of complex water
splitting strategy, which functions at high apparent quantum yield and long term stability
for H2 and O2 evolution, with low activation barrier and moderate overpotential, remain
major challenges in this field. A key issue is to devise an apparatus that exhibits superior
capabilities. It should be able to efficiently separate H2 and O2 evolution with a high rate
and sustain consecutive gas generation for many rounds of photocatalytic cycles.
Numerous schemes have been established by many researchers. However, some
severe problems still remain on despite of the progress made in recent years, including:
(1) Only the UV light of the solar spectrum is utilized, whereas the visible and
infrared irradiations which take a major part of the solar spectrum are underutilized.
(2) An external electric bias is constantly required throughout the water splitting
process, which increases complexity of the water splitting system.
(3) Additional energy consumption will be necessary for the separation of the
evolved H2 and O2 gas after the water splitting process. For the purpose of ensure the
security during the transportation and storage, the purification of the H2 gas is inevitable.
(4) In the case of the water splitting reaction using particulate semiconductor
materials, undesired backward reaction, such as H2-O2 recombination and/or O2
photoreduction, would readily be involved due to the adjacent reaction sites for H2 and O2
evolution.
(5) For the conventional water splitting systems, there is a schottky barrier between
the semiconductor material and the co-catalyst, hindering electron transfer. The water
splitting activity is thus restricted.
(6) There is an absence of an effective evaluation method of the various kinds of
co-catalysts. The most suitable H2 evolution co-catalyst for particular water splitting
reaction environment is also suspensive.
29
(7) The charge carrier migration in the semiconductor is not efficient enough. The
recombination between electrons and holes drastically retards the water splitting reaction.
These issues hamper the exploitation in water splitting reaction system assemblies and
photocatalytic devices for fuel generation. If these challenges can be met, PEC water
splitting may emerge as an economically viable and truly renewable pathway towards the
clean H2 production.
30
1.6 Aim and outline of this thesis
All warning signs in regard to the energy crisis and global warming force us to
consider about the solution to utilize energy which derives from natural resources.
Therefore, the principal aim of this thesis is to make use of renewable energy such as solar
energy and convert it into chemical energy stored in H2 gas by PEC water splitting process.
The body of thesis consists of six chapters including the present chapter 1. This chapter
briefly describes the backgrounds of the study, literature review, mechanism of the water
splitting reaction and the objectives of the study. Chapter 2 introduces the apparatus
designed for hydrogen production using water splitting and experimental details about the
quantitative determination of hydrogen and oxygen evolution. Chapter 3 reports the
plasmon-assisted water splitting using two sides of the same SrTiO3 single-crystal
substrate. The properties of the gold nanoparticles deposited on the SrTiO3 single-crystal
substrates were characterized. The influence of irradiation wavelength and pH value
combinations on H2 and O2 generation were summarized and analyzed. Chapter 4 is
devoted to the co-catalyst effects on hydrogen evolution in the plasmon-induced water
splitting system. Schottky barrier effect between the semiconductor and the co-catalyst
was eliminated. An effective evaluation method of various co-catalysts was proposed.
Chapter 5 presents the plasmon-enhanced water splitting utilizing heterojunction
synergistic effect between SrTiO3 and rutile TiO2. Enhanced water splitting activity was
ascribed to the larger potential gradient between the front and back side of the composite
substrate due to the energy band position difference between SrTiO3 and rutile TiO2. At
the end of the thesis, chapter 6 summarizes the results described in chapter 3-5. This
chapter also describes how this project leads to a future perspective on water splitting
systems for solar fuels generation. Several possibilities are proposed as the further
extension and development of this work.
31
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44
Chapter 2
Plasmon-Induced Water Splitting Using Two Sides of the Same
SrTiO3 Single-Crystal Substrate
2.1 Abstract
A plasmon-induced water splitting system that operates under visible light
irradiation is successfully developed. This system is based on the utilization of both sides
of the same SrTiO3 single-crystal substrate. The most important feature of this system is
that both sides of a strontium titanate single-crystal substrate are used without an
electrochemical apparatus. The water splitting system contains two solution chambers to
separate H2 and O2 evolution. To promote water splitting, a chemical bias was applied by
the regulation of the pH values at the two chambers. The quantity of H2 evolved from the
surface of platinum, which was used as a reduction co-catalyst, was twice the quantity of
O2 evolved from an Au nanostructured surface. Thus, the stoichiometric evolution of H2
and O2 was successfully demonstrated. The hydrogen-evolution action spectrum closely
corresponds to the plasmon resonance spectrum, indicating that the plasmon-induced
charge separation at the Au/SrTiO3 interface promotes water oxidation and the subsequent
reduction of a proton on the backside of the SrTiO3 substrate. It is further elucidated that
the chemical bias is significantly reduced by plasmonic effects, which indicates the
possibility of constructing an artificial photosynthesis system with low energy
consumption. Plasmon-induced water splitting occurred even with a minimum chemical
bias of 0.23 V due to the plasmonic effects based on the efficient oxidation of water and
the use of platinum as a co-catalyst for reduction.
45
2.2 Introduction
To address the global energy issues, the development of a system that converts solar
energy to not only electrical but also chemical energy that can be stored for long periods is
critical.[1-3]
Honda and Fujishima have developed photoelectrochemical water splitting
systems that use a TiO2 photoelectrode irradiated by ultraviolet light.[4, 5]
However, only
approximately 5% of the solar irradiance observed on the Earth’s surface is composed of
ultraviolet radiation (<400 nm), whereas visible light (400-800 nm) and infrared light
(>800 nm) represent 50% and 45%, respectively. Therefore, the extension of light-energy
conversion to longer wavelengths, especially to the visible and near-infrared regions, is
important.[6-8]
The conversion of visible light can be achieved by several methods,
including the use of a Z-scheme electron transfer process,[9, 10]
TiO2 with the addition of
certain dopants,[11-14]
and semiconductor nanoparticles with a bandgap wavelength in the
visible region.[15-18]
To date, semiconductor particles have been used to induce H2 and O2
evolution through the response of such photocatalysts to visible light.[19, 20]
One of the
disadvantages of the use of semiconductor particles in a photocatalytic water splitting
system that requires energy to separate H2 from O2 is that H2 and O2 are evolved in the
same reaction chamber.[21-23]
Recently, the evolution of H2 and O2 in different reaction
chambers has been studied using photoelectrodes fabricated by sintering semiconductor
particles.[24]
Except for the Z-scheme reaction system, such systems do not require cathode
irradiation because hydrogen evolution occurs via a dark reaction. Therefore, the
optimization of a reaction cell design that can effectively utilize light for water splitting is
expected. In this chapter, it is proposed that the simultaneous evolution of H2 and O2 can
be realized without an electric wire connecting the anode and the cathode and with space
conserved for light irradiation on the anode side through the use of two sides of the same
semiconductor substrate. It is a plasmon-induced water splitting system that responds to
visible light, which is based on gold nanoparticles (Au-NPs) loaded onto SrTiO3
single-crystal substrates. The successful separation of H2 and O2 evolution in different
chambers using both sides of the same substrate is also demonstrated. The
46
plasmon-induced charge separation between Au-NPs and oxide semiconductor interfaces
studied here can act as a co-catalyst in water oxidation, which is considered to be a
bottleneck process in water splitting. Thus, this system is promising for artificial
photosynthesis and is expected to be deployed in the future.
47
2.3 Experimental details
2.3.1 Niobium doped strontium titanate single crystals
N-type SrTiO3 has been proven to be efficient anodes for photochemical water
splitting under UV light irradiation. While the large band gaps of SrTiO3 (3.2 eV) resulted
in their low conversion efficiencies of solar energy, thus hindering their practical
applications. For the effective usage of solar energy, many efforts have been made to
develop the visible light responding photoanodes. Recently, the band gaps of n-TiO2 were
effectively reduced by replacing oxygen with nitrogen or carbon to elevate the potential at
the top of the valence band.[11, 25]
Figure 2.1 Energy band structures of TiO2 and SrTiO3
Our group has already successfully observed photocurrent generation and O2
evolution with TiO2 substrate under certain electric bias. Whereas for overall water
splitting, H2 evolution with accurate quantity is also very important. Furthermore, it is
highly desired to realize the overall water splitting without any electric bias. The
conduction band (CB) electrochemical potential of TiO2 is 0 V vs reversible hydrogen
48
electrode (RHE), which is the same as the redox potential of the proton reduction. As a
result, it would be quite difficult for the TiO2 to reduce protons to generate H2 without any
electric bias. While as shown in Figure 2.1, the CB position of the strontium titanate
(SrTiO3) is -0.2 V vs RHE, more negative than the redox potential of the proton reduction,
which makes it take advantage at the H2 evolution. Therefore, the SrTiO3 was chosen as
the catalytic material in this study.
At room temperature, SrTiO3 crystallizes in the ABO3 cubic perovskite structure
where A and B are cations. The lattice constant of SrTiO3 is 0.3905 nm. Its crystal
structure is shown in Figure 2.2. The Ti4+
ions are sixfold coordinated by O2- ions, whereas
each of the Sr2+
ions is surrounded by four TiO6 octahedra. Therefore, each Sr2+
ion is
coordinated by 12 O2- ions. Within the TiO6 octahedra, while a hybridization of the O-2p
states with the Ti-3d states leads to a pronounced covalent bonding, Sr2+
and O2- ions
exhibit ionic bonding character.[26]
Hence, SrTiO3 has mixed ionic-covalent bonding
properties. This nature of chemical bonding leads to a unique structure, which make it a
model electronic material.
Figure 2.2 Crystalline structures of SrTiO3
Figure 2.3 shows the transmittance spectra of the Nb-SrTiO3 (0.05 wt% and 0.5 wt%)
49
single crystals. The transmittance spectra of these single crystals were measured by using
an ultraviolet–visible Spectrometer (Shimadzu UV-3100, Japan). It is obvious that in the
region of UV light absorption, the samples almost show the same absorption edge (about
3.2 eV), corresponding to the electronic excitation from the O 2p state to the Ti 3d state.[27]
In the region of the longer wavelength, the Nb-doped SrTiO3 single crystals show strong
absorption. This phenomenon should partly be ascribed to the optical absorption of free
carriers in the semiconductor. With the larger concentration of carriers, Nb-SrTiO3 (0.5
wt%) shows stronger optical absorption of free carriers in the region of long wavelength
than Nb:SrTiO3 (0.05 wt%). The main features of Figure 2.3 are strong visible light
absorption around 514 nm (c.a. 2.4 eV) for Nb-SrTiO3 (0.05 wt%) and Nb-SrTiO3 (0.5
wt%) single crystals. The enlargement of the transmittance spectrum for Nb-SrTiO3 (0.5
wt%) single crystal is shown in the Figure 2.3 (b). It means that there are intermediate
states within the band gap of Nb-SrTiO3 single crystals.
Taking these aspects into consideration, the SrTiO3 single crystals doped with Nb by
0.05 wt% was chosen as the semiconductor photocatalytic material in this study.
Figure 2.3 (a) The transmittance spectra of the semiconductor single-crystal Nb-SrTiO3
with different doping percentages (0.05 wt% and 0.5 wt%). (b) An enlarged view of (a) in
which the transmittance spectra of 0.5 wt% doped Nb-SrTiO3 is present.
50
2.3.2 Preparation of Au-NPs on a SrTiO3 substrate
Single-crystal strontium titanate (SrTiO3, 0.05 wt% niobium doped, 10 × 10 × 0.5
mm3, Furuuchi Chemical Co.) with a (110) surface was used as a semiconductor substrate
for water splitting. The SrTiO3 substrate as purchased was sequentially rinsed with
acetone, methanol, and deionized water in an ultrasonic bath for 5 min and was dried
under a flow of pure nitrogen. The substrate was subsequently exposed to ozone for 5 min
by excimer lamp (PC-01-H, N-Cobo Co.) irradiation under an O2 atmosphere in order to
remove the organic matter stuck to the surface. A thin gold film (3 nm) was deposited onto
the front side of the SrTiO3 by helicon sputtering (MPS-4000, ULVAC Co.) at a
deposition rate of 1 Å/s and was annealed at a temperature of 800°C for 1 h in a nitrogen
atmosphere to form the Au-NPs onto the SrTiO3 surface.[28]
The Au-NPs on the SrTiO3
surface were observed by field-emission scanning electron microscopy (FE-SEM,
JSM-6700FT, JEOL). The maximum resolution attainable at an electron acceleration
voltage of 15 kV was 1 nm. The extinction spectrum of the Au-NPs was monitored using a
UV/vis spectrometer (UV-3100, Shimadzu Co.).
Figure 2.4 The gold nanoparticles loaded SrTiO3 substrate fabrication and platinum board
decoration process.
51
2.3.3 Construction of the water splitting device
An In-Ga alloy (4:1 weight ratio) paste was applied to the backside of the
Nb-SrTiO3 substrate to form Ohmic contacts. Subsequently, a Pt board (10 × 10 × 0.2
mm3, 99.98%, Nilaco Corporation) was adhered to the backside of the substrate via Ag
paste (D-550, Fujikura Kasei Co.). A schematic illustration of the water splitting system
based on the Au-NP-loaded Nb-SrTiO3 substrate is shown in Figure 2.5. The water
splitting device contained sealed reaction cells with two solution compartments separated
by the SrTiO3 substrate. The Au-NP-loaded surface served as the anode on the front side
of the photoelectrode, which was irradiated by visible light to induce O2 evolution,
whereas a Pt board served as the cathode for H2 evolution on the backside. In the front
chamber, O2 evolution is expected to follow the plasmon-induced charge separation and
the subsequent water oxidation. The evolution of H2 is expected in the back chamber
because of the reduction of protons by photogenerated electrons injected into the
conduction band of Nb-SrTiO3 at the Pt surface, which was used as a reduction
co-catalyst.[29]
To adjust the chemical bias between the H2- and O2-evolution chambers,
the pH was regulated using arbitrary concentrations of hydrochloric acid (HCl) and
potassium hydroxide (KOH) aqueous solutions. The volumes of H2- and O2-evolution
chambers are 600 and 230 µL, respectively. To maintain the charge balance between the
two chambers, a salt bridge with 2 wt% agar was used. The pH values of the solutions
were examined using a pH meter (AS600, AS ONE Co).
Figure 2.5 A schematic illustration of the water splitting device using Au-NPs loaded
Nb-SrTiO3 photoelectrode.
52
In order to keep the charge and ion balance between the two reaction chambers, a
conventional salt bridge was used. The 100 mL potassium chloride (KCl) aqueous solution,
which contained 30 g KCl (nearly saturated condition), was dissolved by agar powder
with 2 wt%.[30]
The solution was then injected into a colorimetric tube, and heated in water
bath to keep the temperature steady at 95℃ , so as to prevent the solution from
solidification. A silica capillary tube with an inner diameter of 0.2 mm was inserted into
the agar solution afterwards. Due to the capillary effect, the agar solution successfully
entered into the silica capillary tube.[31]
Subsequently, the tube was taken out of the agar
solution. After the refrigeration of the agar solution in the tube to the room temperature, a
salt bridge was acquired. The tips of the salt bridge were inserted into the two reaction
chambers respectively during the water splitting process. During the water splitting
process, protons transferred from the front side to the back side of the reaction system
through this salt bridge in order to keep the charge balance between the two reaction
chambers. The salt bridge has the same function as a proton exchange membrane, e.g.
nafion film.[32, 33]
Figure 2.6 The installation for the fabrication of the salt bridge and its assembly to
the water splitting reaction cell.
53
2.3.4 Quantitative determination of hydrogen evolution
The amount of evolved H2 was quantitatively determined by a gas chromatograph
equipped with a thermal conductivity detector (GC-TCD 2014, Shimadzu Co.). The area
counts of the peaks and the identity of the gas were analyzed from the calibrated carrier
times. The HCl aqueous solution was bubbled with N2 for 60 minutes before each
experiment in order to remove the residual O2 in the solution. N2 gas was injected into the
H2 evolution side, as reference gases for the yield calculations. The GC-TCD was
equipped with a 6.0-m packed column (Shincarbon ST 50/80, Shimadzu Co.), and the
carrier gas was Ar with a flow rate of 30 mL/min. The gas evolved (10.0 μL) from the
backside chamber was injected. The column and sample injection temperatures were
120°C and 200°C, respectively. The detector temperature was set to 200°C.
The calibration curve of H2 and the reference gas N2 is shown in the Figure 2.8.
According to this calibration, the H2 detection limit of our GC-TCD device is 5.6 × 10-5
mol dm-3
or less. Since the volume of the sample injected into the GC-TCD is 10 μL, the
H2 detection limit of our GC-TCD device is estimated to be 0.56 nmol.
Figure 2.7 Gas chromatogram of typical sample extracted from the H2 evolution side
after the water splitting process.
54
Figure 2.8 The calibration curve of H2 using N2 as a reference gas.
2.3.5 Quantitative determination of oxygen evolution
The amount of evolved O2 was quantitatively determined by gas
chromatography-mass spectroscopy (GC-MS 2010-plus, Shimadzu Co.). The area counts
of the peaks and the identity of the gas were analyzed from the calibrated carrier times.
The KOH aqueous solution on the O2 evolution side of the cell was labeled with 18
O-water
(17.4 atom % isotopic purity) in order to quantify the oxygen evolution. The KOH
aqueous solution was bubbled with Ar for 60 minutes before each experiment in order to
remove the residual O2 in the solution. Ar gas was injected into the O2 evolution side, as
reference gas for the yield calculations. The GC-MS used to separate and determine the O2
was equipped with an electron ionization (EI) source and a 30.0 m RT-Msieve 5A column
(RESTEK); He at a flow rate of 42 mL/min was used as the carrier gas. The gas evolved
(5.0 μL) from the front side of the photoelectrode was injected in the split mode, with a
split ratio of 30, and the selected ion monitoring (SIM) mode was used for the detection of
O2. The column and sample injection temperatures were maintained at room temperature.
The EI ionization source temperature was set to 200°C.
The mass-to-charge ratio (m/z) of 28, 32, 34, 36, and 40 were determined by the gas
chromatography-mass spectrometry (GC-MS) spectra. A typical GC-MS chromatogram of
55
the sample from the water splitting device after visible light irradiation is shown in Figure
2.9. The (m/z) of 28, 32, 34, 36, and 40 are corresponding to 28
N2, 32
O2, 34
O2, 36
O2 & 36
Ar,
and 40
Ar gas chromatogram respectively. The area of gas chromatogram was used for the
calculation of gas concentration.
The peak of the 36
O2 was submersed in that of the 36
Ar, which was an isotope of the
reference gas used for quantitative determination. Because it was difficult to distinguish
these peaks from each other, the 36
O2 was not used to calculate the amount of O2 gas
evolution. In order to prevent the contamination from the air during the measurement, 32
O2
was not used in the calculation either. Thus, the 34
O2 gas chromatogram was used for
quantitative determination of the oxygen evolution, which was then compared with the
natural abundance ratio. The calibration curve of 34
O2 using 40
Ar as a reference gas is
shown in Figure 2.10. According to this calibration, the 34
O2 detection limit of our GC-MS
device is 6.0 × 10-6
mol dm-3
or less. Since the volume of the sample injected into the
GC-MS is 5 μL, the 34
O2 detection limit of our GC-MS device is estimated to be 0.03
nmol.
The mass-to-charge ratio (m/z) of 34 was determined from the gas
chromatography-mass spectrometry (GC-MS) spectra. The gas of m/z 34 is a kind of
oxygen isotope gas, which contains one 16
O and one 18
O atom. The gas chromatogram
intensity of the m/z of 34 increased with irradiation time.
Figure 2.9 (a) A typical GC-MS chromatogram of the sample from the water splitting
56
device after the anode side chamber was irradiated with visible light. Intensity was
normalized to m/z 40. (b) A zoomed-in view of the area in which argon and oxygen peaks
are present.
Figure 2.10 The calibration curve of 34
O2 using 40
Ar as a reference gas.
57
2.4 Results and discussion
2.4.1 Characterization of Au-NPs
A top view scanning electron microscope image of the Au-NPs on Nb-SrTiO3 single
crystal substrates was used for statistical analysis of the Au-NPs particle size distribution
based on the usage of free software ImageJ (http://rsb.info.nih.gov/ij/). With prolonged
annealing, the gold thin film grows in shape to give a more ordered structure as reported
previously.[34]
The scanning electron microscope image and Au-NPs particle size
histograms distribution of Au-NPs/SrTiO3 were shown in the Figure 2.11.
Figure 2.11 The scanning electron microscope top view image (a) and the particle size
histograms distributions (b) of Au-NPs on Nb-SrTiO3 photoelectrode after annealing at
800°C in a nitrogen atmosphere. The scale bars represent 100 nm.
The SEM images confirmed that the gold films transformed to a discontinuous
nanoparticle structure after annealing at 800°C in a nitrogen atmosphere, and the
interparticle spacing was comparable to the nanoparticle size. The diameter of the Au-NPs
distributes nearly symmetrically with the average size at around 52 nm, and the standard
deviation for the structural size was estimated to be 19 nm. The surface area coverage of
gold nanoparticles is approximately 26 % on the SrTiO3. Typical scanning transmission
58
electron microscope (STEM) images of Au-NPs cross-section and top view were shown in
Figure 2.12. The shape of Au-NPs on SrTiO3 was spherical segmental structure with
average height of about 32.7 nm. The Au-NPs tightly contact with TiO2 surface.
Figure 2.12 The transmission electron microscope cross section view with different
magnification (a), (b) and top view (c) images of Au-NPs on Nb-SrTiO3 photoelectrode
after annealing at 800°C in a nitrogen atmosphere. The scale bars represent 100 nm in all
images.
Typical XPS spectra characterization of Au-NPs on SrTiO3 substrate after annealing
at 800°C in a nitrogen atmosphere is shown in Figure 2.13. The Au 4f5/2 and 4f7/2 peaks
were centered at approximately 87.5 eV and 83.8 eV, which are in good accordance with
the standard values reported.[35]
The X-ray diffraction patterns of Au-NPs on SrTiO3 after
annealing at 800°C in a nitrogen atmosphere is shown in Figure 2.14. The peak that
represents the gold (111) crystal facet was clearly observed, indicating the crystalline
nature of the gold nanoparticles. Figure 2.15 shows the extinction spectrum of the Au-NPs
on the Nb-SrTiO3 substrate. A localized surface plasmon resonance (LSPR) band peaking
at a wavelength of 630 nm is clearly observed.
59
Figure 2.13 Partial XPS spectra characterization of Au-NPs on SrTiO3 after
annealing at 800°C in a nitrogen atmosphere.
Figure 2.14 X-ray diffraction patterns of Au-NPs on SrTiO3 after annealing at
800°C in a nitrogen atmosphere.
100 95 90 85 80 75 70
Au 4f7/2
Inte
nsi
ty (
a.u
.)
Binding Energy (eV)
Au 4f5/2
20 30 40 50 60 70 80
0
50000
100000
150000
200000
250000STO (220)STO (110)
Counts
2θ (degree)
Au-NP on STO
Au (111)
60
Figure 2.15 Extinction spectrum of the Au-NPs on Nb-SrTiO3 after annealing at
800°C in a nitrogen atmosphere.
2.4.2 Numerical simulations of Au-NPs on SrTiO3
The extraordinarily powerful localized electromagnetic field that generated by
localized surface plasmon resonance may have a strong impact on the water splitting
activity enhancement. Nevertheless, the experimental measurement of the localized
electromagnetic field enhancement is very difficult. Therefore, the computational
simulation of the near-field intensity enhanced by the gold nanoparticles is an efficient
method to address this issue.
The finite difference time domain (FDTD) simulation is a numerical analysis
technique which is used for modeling the computational electrodynamics. This method is
one of the many categories of the general class of grid-based differential time-domain
numerical modeling methods. As a versatile modeling technique, FDTD is used to solve
Maxwell's equations and provide animated displays of the electromagnetic field
movement through the model. An increasing number of researches are using FDTD
technique to investigate optical properties of certain noble metal nanostructures in recent
years because the electric field intensity pattern is readily available in real space and the
algorithm is independent of the particular structure to be solved. Additionally, noble metal
450 500 550 600 650 700 750 800 850
0.00
0.05
0.10
0.15
0.20
0.25
0.30
Extin
ctio
n
Wavelength (nm)
61
nanostructures have drawn considerable attention because of the existence of surface
plasmon resonance, which give rise to resonant effects and field enhancement leading to
many interesting applications.
To obtain a more rigorous understanding of the mechanism of water splitting
activity enhancement, the FDTD simulation method (Lumerical) was thus adopted to
simulate the electric field intensity distribution of gold nanostructures on SrTiO3 substrate
under the LSPR excitation. These simulations are based on the transmission electron
microscope (TEM) image of the Au nanoparticle and SrTiO3 surface, as shown in Figure
2.12, which is used to define the spatial extent of the Au nanoparticle islands in our
simulation. To calculate the field distribution, the following parameters were used: the
refractive index of the SrTiO3 substrate was set as 2.4, the optical constants for gold was
taken from Johnson and Christy, and the mesh accuracy was set at 0.5 nm.
Maps of the near-field electromagnetic intensity distribution patterns localized
around gold nanostructures on SrTiO3 at the maximum wavelength of the extinction
spectra were obtained from the FDTD simulation method in both the x-z and x-y planes,
as shown in Figure 2.16. For field enhancement, hemispherical shaped gold nanostructures
with diameters of 52 nm were used under periodic boundary conditions. In the x-z plane,
the intensity detector is located at the sphere center of the gold nanostructure and overlaps
the x axis. In the x-y plane, the detector is located at the interface between the gold
nanostructure and the SrTiO3 substrate. Notably, from the simulation, the electromagnetic
field intensity is greatly enhanced around the common boundary between gold, SrTiO3
substrate, and aqueous solutions, with the highest enhancement factor of nearly 500,
compared with the incident electric field at the SrTiO3 surface. This electromagnetic
response is dominated by local hot spots. This means that the electron hole pair generation
rate is 500 times that of the incident electromagnetic field. Thus, an increased amount of
charge is induced locally in the SrTiO3 because of the local field enhancement of the
plasmonic gold nanoparticles. Such kind of highly localized electromagnetic field was
supposed to play a key role for the electron excitation and the subsequent charge
62
separation. While there is no way to measure the electronhole pair generation rate in an
isolated plasmonic hot spot, the present work measuring plasmon-enhanced water splitting
provides perhaps the most direct measurement of this, since every two electrons produce
one hydrogen molecule.
Figure 2.16 FDTD simulation showing the electric field intensity distribution around the
gold nanostructure in the x-z (a) and x-y (b) planes. The dashed rectangle represents the
periphery of the gold nanostructure. The scale bar shows the enhancement factor.
2.4.3 Influence of irradiation wavelength on H2 and O2 generation
Figure 2.17 (a) depicts the irradiation time dependence of H2 and O2 evolution in the
backside and front-side chambers, respectively. Experimental about the quantitative
determination of H2 and O2 evolution was described in the supporting information. The
pH value was adjusted to 1 on the H2-evolution side, whereas the pH value on the
O2-evolution side was adjusted to 13 (i.e., the chemical bias was equivalent to 710 mV). A
xenon light spectrally filtered over the wavelength range of 450 nm to 850 nm was used to
irradiate the Au-NPs and induce LSPR. Under the irradiation conditions, the evolution of
H2 and O2 increased linearly with increasing irradiation time. As for the time dependence
of H2 and O2 evolutions, linearity was maintained in irradiation time, and it was not a
quantity of evolution to the extent that pH changes. Actually, it has been confirmed that
63
the pH value did not change before or after the irradiation. In a separate experiment, it has
also been confirmed that neither H2 nor O2 was evolved from a Nb-SrTiO3 substrate
without Au-NPs under the same irradiation conditions. No production of H2 or O2 was
observed in the absence of irradiation for an extended period (6 h), even when the
Au-NP-loaded Nb-SrTiO3 substrate was used. Figure 2.17 (a) shows that the quantity of
H2 evolved from the surface of Pt, which was used as a reduction co-catalyst, is twice the
quantity of O2 evolved from the Au nanostructured surface. Therefore, the stoichiometric
evolution of H2 and O2 was clearly demonstrated in the water splitting system based on the
Au-NP-loaded Nb-SrTiO3 single-crystal substrate.
Figure 2.17 (a) An irradiation time dependence of H2 (red circle) and O2 (blue circle)
evolution obtained in back and front side chamber, respectively. (b) The action spectrum
of apparent quantum efficiency with several wavelength regions using a histogram. The
solid line indicates LSPR band already shown in Figure 2.15.
The histogram in Figure 2.17 (b) shows the action spectrum of apparent quantum
efficiency (AQE). The pH conditions used were a pH of 1 for the H2-evolution side and a
pH of 13 for the O2-evolution side. Sectionalized yields of the AQE dependent on the
irradiation wavelength was measured with the increment as 100nm. In the 600 ± 50 nm,
700 ± 50 nm, and 800 ± 50 nm wavelength regions, the evolution efficiency (mol/h) of H2
is in approximate agreement with the segmented integral area of the the LSPR band of the
64
extinction spectrum indicated by the solid line in Figure 2.17 (b), whereas the evolution
efficiency of H2 in the 500 ± 50 nm wavelength region is higher than that indicated by the
spectrum of the Au-NPs on the Nb-SrTiO3. This result indicates that H2 and O2 evolution
was induced not only by LSPR excitation but also by the direct excitation of the interband
transition from the d-bands to the sp-conduction band of gold in the 500 ± 50 nm
wavelength region. Thus, the H2-evolution efficiency in the shorter-wavelength region is
higher than that in the longer-wavelength region. Notably, the water splitting is closely
related to the LSPR excitation because the AQE is strongly dependent on the LSPR band.
In the present system, the number of active sites or molecules of the photocatalyst is
impossible to be estimated. Therefore, turnover number is unavailable as an index to
evaluate the performance in this study. In addition, since the UV irradiation was cut off in
order to investigate the visible response, solar energy conversion efficiency is also
unaccessible in this research.
2.4.4 Influence of pH value combinations on H2 and O2 generation
To further understand this system in detail, a pH-dependence experiment was
performed to investigate the effect of the chemical bias on the water splitting. In the
experiment, a xenon light spectrally filtered over the wavelength range of 550 nm to 650
nm with an intensity of 0.32 W/cm2 was used for the LSPR excitation. Figure 2.18 (a)
indicates the representative irradiation time dependence of H2 and O2 evolution at the pH
combination of 1 and 13. The evolution of both H2 and O2 increases linearly with
increasing irradiation time, and the quantity of H2 evolved is twice that of O2 evolved,
which is analogous to the results in Figure 2.17 (a). Figure 2.18 (b) shows the pH
dependence of the H2 and O2 evolution efficiency. The pH value on the O2-evolution side
was fixed at 13, as indicated by the blue background in Figure 2.18 (b), which is the
condition that preferentially induces water oxidation. The evolution efficiency of H2 is
twice that of O2 at the observed pH value. However, the evolution efficiency of both H2
and O2 gradually decreased with increasing pH value on the H2-evolution side, and no
65
production of H2 or O2 was observed at a pH value of 4. Therefore, a chemical bias was
required in the water splitting in this system of at least 0.59 V, which corresponds to the
difference between pH 3 and pH 13. However, a pH value of 1 was fixed on the
H2-evolution side, as indicated by the red background in Figure 2.18 (b), which is the
condition that preferentially induces H2 evolution. Similarly, the evolution efficiency of
H2 was twice that of O2 at the observed pH value. In contrast, the evolution efficiency of
both H2 and O2 gradually decreased with decreasing pH value on the O2-evolution side.
However, the evolution of both H2 and O2 was still observed, even at a pH of 6.8 using a
pure water. In addition, neither H2 nor O2 evolution was observed at a pH of 6. Therefore,
in this system, a chemical bias was required in the water splitting of at least 0.34 V, which
corresponds to the difference between pH 1 and pH 6.8. Therefore, the chemical bias
required for the water splitting changes as the fixed pH value in the chamber changes.
When the pH value at the cathode was fixed to 1 and the pH at the anode was
increased from 6.8 to 10, hydrogen was evolved due to the reduction of protons at the
cathode, whereas oxygen was evolved due to the oxidation of water molecules via a
four-electron reaction. Therefore, the water splitting reaction did not exhibit a significant
pH dependence. When the pH at the anode was increased from 11 to 13.5, oxygen was
evolved due to the oxidation of water molecules and OH- ions. The amount of evolved
gases increased gradually as the pH was increased at the anode. Similarly, when the pH at
the anode was fixed at 13 and the pH at the cathode was gradually increased from 1, the
quantity of the evolved gases decreased because the proton concentration at the cathode
decreased with increasing pH values. Neither gas was detectable at pH 4 on the cathode
side. On the basis of these results, it is hypothesized that hydrogen evolution was the
rate-limiting process of the present water splitting reaction. Because water splitting did not
proceed when the pH at the anode was 6, the minimum chemical bias in this system was
estimated to be 230 mV, which corresponds to the combination of pH 3 (cathode side) and
pH 6.8 (anode side). Although water oxidation is the rate-limiting process in a typical
water splitting system, it is concluded that the water splitting proceeded at a relatively low
66
chemical bias of 230 mV because the plasmon-induced charge separation efficiently
oxidized the water.
Figure 2.18 (a) An irradiation time dependence of H2 (red circle) and O2 (blue circle)
evolution at the pH combination of 1 and 13 under the conditions that the xenon light
spectrally filtered to the wavelength from 550 nm to 650 nm with an intensity of 0.32
W/cm2 was irradiated. (b) The pH dependence of the H2 (closed circle and square) and O2
(open circle and square) evolution efficiency under the conditions that the pH value in the
H2 evolution side is fixed at 1 as plotted on red background and the pH value in the O2
evolution side is fixed at 13 as plotted on blue background, respectively.
To further explore the limiting pH conditions for H2 and O2 evolution, the pH values
on the H2- and O2-evolution sides were fixed at 3 and 6.8, respectively, which are the
minimum acidic and alkaline conditions observed in the previous experiments to promote
evolution of H2 and O2, respectively. The irradiation time dependence of H2 and O2
evolution is shown in Figure 2.19(a). The results confirm that the evolution of both H2 and
O2 increased approximately linearly with increasing irradiation time and that the
efficiency of H2 evolution was twice that of O2 evolution. The pH dependence is shown in
Figure 2.19(b), which is summarized as being analogous to Figure 2.18(b). The evolution
efficiency of both H2 and O2 gradually decreased with increasing pH on the H2-evolution
side, and no production of H2 or O2 was observed at pH 4. When the pH value was set to 4
on the H2-evolution side, the water splitting did not proceed at either pH value on the
67
O2-evolution side. This result indicates that the reaction rate of hydrogen evolution is the
rate-determining process in water splitting. In addition, the absolute efficiency is
significantly lower than the previous data because of the insufficient chemical bias applied
to that system. In the case where the pH value on the H2-evolution side was fixed, water
splitting was induced, even at a pH combination of 3 and 6.8, which corresponds to a
minimum chemical bias of 0.23 V in this plasmon-assisted water splitting system.[36]
To
the best of the authors’ knowledge, this chemical bias is the smallest value reported for a
water splitting system driven by visible-light irradiation.
Figure 2.19 (a) An irradiation time dependence of H2 (red circle) and O2 (blue circle)
evolution at the pH combination of 3 and 6.8. (b) The pH dependence of the H2 (closed
circle and square) and O2 (open circle and square) evolution efficiency under the
conditions that the pH value in the H2 evolution side is fixed at 3 as plotted on yellow
background and the pH value in the O2 evolution side is fixed at 6.8 as plotted on green
background, respectively.
2.4.5 Mechanism for the plasmon-assisted water splitting reaction
The pH dependence experiments clearly demonstrated that the pH dependence of
water splitting exhibits an asymmetrical response. The mechanism for water oxidation is
considered to rely on the adsorption of OH- onto the surface of SrTiO3, close to the
Au-NPs. In addition, the efficiency of O2 evolution is strongly dependent on the
68
concentration of OH-, as defined by the pH value, because the adsorbed hydroxyl ions
must be oxidized by multiple electron holes to evolve oxygen.[37]
However, under neutral
conditions, such as pH 6.8, the surface concentration of OH- is lower than that under
alkaline conditions. Water molecules must dissociate to form adsorbed OH- on the surface
of SrTiO3, thereby resulting in the observation that the reaction rate of water oxidation is
lower than that of OH- oxidation. Notably, the effective water-splitting process proceeds
under neutral conditions in the present system, which suggests that water molecules could
be directly oxidized by the plasmon-induced water splitting system. Thus, the efficient
oxidation of water and OH- also requires highly concentrated electron holes at a local site
because multiple electron transfer processes are required with two water molecules or four
OH- groups. The possibility exists that the LSPR generates multiple holes at the
plasmonically enhanced optical near-field because of an efficient charge separation and
that the multiple holes trapped at the surface states of SrTiO3 near the hot site might be
stored at a local site of the SrTiO3. The stored multiple holes confined at a local site of the
SrTiO3 may be able to accelerate the oxidation of water or OH- and the subsequent
evolution of oxygen.
Figure 2.20 A schematic diagram of the hot sites near the interface between the
Nb-SrTiO3 substrate and the Au-NPs.
Figure 2.21 illustrates the energy diagram of the plasmon-induced water splitting
system based on the Au-NP-loaded SrTiO3 photoelectrode at the pH combination of 3 and
6.8. It is hypothesized that the plasmon resonance is first induced by visible and
69
near-infrared light, and the enhanced optical near-field excites an electron from the gold
nanoparticles or from the surface-state electron of the Nb-SrTiO3. The excited electron is
transferred to the conduction band of the Nb-SrTiO3. The electron that arrived at the back
of the substrate reduces a proton on the Pt surface and hydrogen is evolved from the
cathode. Conversely, the hole left behind at the Au/SrTiO3/water interface oxidizes water
or OH- via multi-electron transfer, and oxygen is evolved from the anode.
[38] Thus,
plasmon-induced water splitting was clearly demonstrated, and the efficient water
oxidation due to the plasmon effect reduced the chemical bias by 0.23 V.
Figure 2.21 Energy diagram of the plasmon-induced water splitting system using Au-NPs
loaded SrTiO3 substrate at the pH combination of 3 and 6.8. The flat band potential of
SrTiO3 at pH 6.8 was estimated as -0.601 V vs. SHE because the potential of the
conduction band of SrTiO3 is known to be -0.2 V vs. SHE at pH 0. The difference in the
potential of 0.401 V is due to pH difference.
The water oxidation appears to proceed efficiently because the hole does not remain
in the Au-NPs. Moreover, multiple holes are trapped in the surface states of Nb-SrTiO3 in
a spatially selective nanospace near the Au-NPs/Nb-SrTiO3/water interface, thus allowing
for oxidization of the water molecules. Therefore, it can be concluded that the
plasmon-induced charge separation behaves like a co-catalyst for oxygen evolution. It is
70
reasoned that the generated holes did not remain in the Au-NPs because the Fermi levels
(Ef) of Nb-SrTiO3 and Au coincide when the Au-NP contacts the surface of Nb-SrTiO3. It
is known that Ef exists slightly below the conduction band energy of Nb-SrTiO3. Because
the generated holes might easily migrate to the Ef, the holes will lose the capability of
oxidizing water in a thermodynamically favored manner because the potential difference
between the flat band potential and Ef is approximately 0.9 V when Au is in contact with
TiO2. The main characteristic of the water splitting system is that hydrogen and oxygen
are produced separately and can be removed from the different electrolysis chambers.
Additionally, only the Au-NP side needs to be irradiated, which reduces the area required
for light irradiation because the reduction of the proton is a dark reaction.
2.4.6 Stability of the plasmon-assisted water splitting system
The water splitting experiment with a longer time irradiation was carefully
performed to check its stability. The irradiation time dependence of H2 and O2 evolution
with a pH combination of 3 and 6.8 is shown in Figure 2.22. The linear relationship of
both H2 and O2 evolution was obviously observed even with an irradiation of 48 hours.
Thus, a stable plasmon-assisted water splitting system was constructed.
Figure 2.22 The irradiation time dependence of H2 and O2 evolution with a pH
combination of 3 and 6.8. The data from 1 to 6 as an irradiation time was taken from
Figure 2.18 (a).
71
2.5 Conclusions
In conclusion, a stable and simple plasmon-induced water splitting system without
an external electrochemical apparatus was successfully developed by using two sides of
the same SrTiO3 single-crystal substrate. The reaction cell involved no electric bias.
Instead, the pH value regulation is adopted. Namely, the electric potential has been
successfully substituted with chemical potential in the photocatalytic water splitting
reaction. The huge advantage using plasmonic Au nanostructures is stable over long time
unlike molecular sensitizers and its plasmon resonant wavelength can be tuned by simply
changing their shape and/or size to cover a large part of the solar spectrum. A
stoichiometric evolution of H2 and O2 was simultaneously obtained from two separate
solution chambers. The quantity of the evolved gases linearly increased with the
irradiation time. Solar energy has been successfully converted into chemical energy and
stored in the form of hydrogen gas. The separate evolution of H2 and O2 is expected to
suppress the recombination of the two gases. Even the irradiation of the unprecedented
long wavelength from 750 nm to 850 nm succeeded in water splitting. The mechanism for
the water splitting device occurs through plasmon-induced charge separation at the
Au-NP/SrTiO3 interface, thereby promoting water oxidation and subsequent reduction of a
proton on the backside of the SrTiO3 substrate. The H2 and O2 generation efficiency is
highly dependent on the pH values of the solution environments. The pH dependence
experiments revealed that the chemical bias is substantially reduced by plasmonic effects
up to 0.23 V because of efficient water oxidation. Although the apparent quantum
efficiency is still low (4.4 × 10-4
% at 600 nm), these results indicate the possibility of
constructing an efficient artificial photosynthesis system that responds to visible and
near-infrared light and does not need the chemical bias through the combination of an
efficient co-catalyst for H2 evolution on the backside of a SrTiO3 substrate as well as
understanding the detailed mechanism.
72
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[25]. Khan, S. U. M., Al-Shahry, M. and Ingler, W. B., Efficient Photochemical Water Splitting by a
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Water Oxidation with a Gold Nanoisland-Loaded Titanium Dioxide Photoelectrode. The Journal of Physical
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Electrochemical Society 2002, 149 (3), A256-A261.
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[34]. Ming, T., Suntivich, J., May, K. J., Stoerzinger, K. A., Kim, D. H. and Shao-Horn, Y., Visible Light
Photo-oxidation in Au Nanoparticle Sensitized SrTiO3:Nb Photoanode. Journal of Physical Chemistry C
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[35]. Nam, S. H., Kim, M. H., Hyun, J. S., Kim, Y. D. and Boo, J. H., XPS Analysis by Exclusion of
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76
Chapter 3
Co-catalyst Effects on Hydrogen Evolution in the
Plasmon-Induced Water Splitting System
3.1 Abstract
Recently great progress has been achieved in the development of
photoelectrochemical (PEC) water splitting. Especially, water splitting systems that
respond to visible light have received considerable attention in the past decade. The water
splitting systems that respond to visible light have been developed according to metal ion
doping to semiconductor, Z-scheme process, and dye or plasmon sensitization. Although
the progress in plasmon-induced water splitting system made in recent few years, the
water splitting efficiency is still low. It is well known that loading proper co-catalysts on
semiconductors (as light harvesters) can significantly enhance the activities of PEC water
splitting reactions. Therefore, it is of significance to establish a system with rational
design to precisely evaluate the capacity of different kinds of co-catalysts. A lot of
studies were performed using n-type semiconductor particles system to elucidate
co-catalyst effects so far. In these studies, however, it is difficult to evaluate only the
catalytic activity of H2 and O2 evolutions as following reasons; 1) An electron injected
into the conduction band of semiconductor is hard to transfer to the H2 evolution
co-catalyst because Schottky barrier can be readily formed when a metallic co-catalyst
for H2 evolution contacts the n-type semiconductor, hindering the performances of the
co-catalyst from being comprehended. 2) There is a possibility that a reverse reaction of
water splitting occurs and these co-catalysts also promote reduction of the evolved O2. In
order to tackle these factors, a facile plasmon-induced water splitting system using gold
nanoparticles (Au-NPs) loaded strontium titanate (SrTiO3) single crystal substrate was
77
developed. In this chapter, the co-catalyst effect on hydrogen evolution in the
plasmon-induced water splitting was investagated. To eliminate the adverse effect of the
Schottky barrier, a Pt board was stick on the hydrogen (H2) evolution side of the SrTiO3
substrate via In-Ga alloy to obtain ohmic contact between semiconductor and metal or
metal oxide co-catalysts. The water spitting yield with this SrTiO3/Pt composite substrate
was remarkably enhanced as compared to that with the Pt thin film without In-Ga Alloy
as H2 evolution co-catalyst. The importance of the ohmic contact for the H2 evolution in
the plasmon-induced water splitting system was thus successfully demonstrated.
Subsequently, the Pt board was decorated with a noble metal or their corresponding metal
oxide as a co-catalyst for H2 evolution. Enhanced evolution of H2 and O2 with
stoichiometric ratio was obviously demonstrated with all kinds of co-catalysts. As the
result, among the co-catalyst materials examined, rhodium thin layer with a thickness of
2 or 3 nm deposited on platinum board exhibited relatively high performance as a 3-fold
increment compared with the absence of any metal or metal oxide co-catalyst thin layer
for this application. Furthermore, the evolution of H2 and O2 were successfully separated
according to using two sides of the same SrTiO3 substrate. The separate evolution of H2
and O2 was supposed to suppress the undesirable reverse reactions of water splitting such
as H2–O2 recombination and/or photoreduction of O2.
78
3.2 Introduction
In order to realize a substitution for the fossil fuels, the development of clean,
environmental friendly, and sustainable energy sources has drawn considerable attention
by many researchers. Currently, it has become common sense that solar energy will play a
key role in the development of new energy sources since it is abundant, clean and
especially renewable. Hydrogen has attracted significant interest as a renewable energy
carrier offering both high-energy capacity and minimal environmental impact. As a
sustainable approach for new energy sources, photocatalytic hydrogen production utilizing
solar energy is a promising strategy.[1]
Photoelectric conversion and the photoelectrochemical water splitting has been of
great interest since the early 1970s after the first demonstration using a titanium dioxide
(TiO2) photoelectrode under ultraviolet radiation by Fujishima and Honda.[2]
Nevertheless,
one drawback of TiO2 is that it can only be excited by ultraviolet light, i.e., with
wavelengths shorter than ca. 400 nm. Therefore, only a very small portion of solar
radiation (3–5%) can be utilized to drive such chemical reactions. Thus, extension of its
absorption wavelength range to the visible region becomes an important issue. Numerous
attempts have been made afterwards to extend the cutoff wavelength of the water splitting
system. To date, utilization of visible light has been attained by doping,[3]
defect creation,[4]
and organic dye sensitization.[5]
Thereinto, plasmon-induced water splitting realized by
noble metal nanoparticles decorated on catalytic semiconductor materials possesses
unique advantages, as has been reported by some researchers.[6, 7]
Previously, our research
group successfully demonstrated plasmon-enhanced photocurrent generation and water
oxidation through irradiation with visible and near-infrared light using a TiO2 single
crystal photoelectrode loaded with Au-NPs.[8]
The solar to chemical energy conversion efficiency is still low and far from practical
application up until now, although many materials have been found to be capable of
performing the water splitting reaction. The reason might be that there are three crucial
steps for the water splitting reaction which is considered to be not yet efficient: solar light
79
harvesting, charge separation and transportation, and the catalytic reduction and oxidation
reactions. Among these problems, in this chapter, the co-catalyst effects concerning with
the multiple electron transfer process is discussed.
As a thermodynamically uphill reaction, water splitting requires the transfer of
multiple electrons, making it one of the most challenging reactions in chemistry. It is well
known that adequate co-catalysts loaded semiconductors significantly enhance the
activities of the water splitting. For semiconductor-based PEC systems, loading oxidation
and/or reduction co-catalysts can facilitate oxidation and reduction reactions by providing
the active sites and reaction sites while suppressing the charge recombination and reverse
reactions. The important roles of co-catalysts in PEC water splitting reactions have been
under investigation for a long time. Domen et al. have reported multiple co-catalysts to
enhance the water-splitting activity, including co-catalysts for the reduction of water to
form H2 such as Pt, Rh, and co-catalysts for the oxidation of water to form O2 such as IrO2,
Mn3O4, RuO2.[9, 10]
Based on the former work, it is already known that the photocatalytic
activity is highly dependent on the kind, size and morphology of the co-catalysts.
Nevertheless, the intrinsic properties of many kinds of co-catalyst and their interaction
mechanisms with catalytic semiconductor materials are still not so clear at the present time.
Thus, it is of special significance to evaluate the capacity of various co-catalysts and to
acquire an in-depth understanding of their function in the process of the PEC water
splitting reactions. However, in most conventional photocatalyst architectures, it is
difficult to evaluate co-catalyst effect for hydrogen (H2) evolution correctly in the water
splitting system using semiconductor particles as following reasons. As for H2 evolution, it
becomes problem that Schottky barrier formed by loading metal on the surface of
semiconductor makes electron transfer rate from the conduction band of semiconductor to
the metallic co-catalyst slow as result in increasing the possibility to induce the back
electron transfer reaction. Namely, it is not understandable because not only co-catalyst
effects but also Schottky barrier effect is included in the experimental results. In addition,
it also becomes problem that a reverse reaction of water splitting such as H2–O2
80
recombination to form H2O and photoreduction of O2 simultaneously induced in the
semiconductor particles system because the co-catalysts also promote the reduction of the
evolved O2. Therefore, the evaluation of co-catalyst effect for H2 evolution might not be
simple. In the previous chapter, a facile artificial photosynthesis system using the In/Ga
alloy to eliminate the Schottky barrier was described.[11]
The evolution of H2 and O2 has
been successfully separated according to using two sides of the same SrTiO3 substrate
which work as cathode and anode, respectively.
Liao et al. reported that cobalt oxide (CoO) nanoparticles can carry out overall water
splitting with a solar-to-hydrogen efficiency of around 5%.[12]
However, the H2 and O2
were evolved at the same site of the identical nanoparticle material. Hence, the undesired
recombination between H2 and O2 was thus inevitable. Luo et al. described a low-cost
water splitting cell combining a solution-processed perovskite tandem solar cell and a
bifunctional earth-abundant catalyst with a solar-to-hydrogen efficiency of 12.3%.[13]
Despite the exceptionally high efficiency, external electric bias was constantly required in
the water splitting process.
Herein, it is proposed that the stoichiometric evolution of H2 and O2 can be realized
by using two sides of the same semiconductor substrate without any external electric bias.
Chemical potential was employed by adjusting the pH value difference between the two
reaction chambers, in order to substitute the conventional electrical potential as a driving
force to promote the water splitting reaction.
In this chapter, the plasmon-induced water splitting system that responds to visible
light using Au-NPs loaded SrTiO3 single crystal substrate is presented. Electron transfer
from the semiconductor material to the cathode was facilitated by the Ohmic contact,
which was formed by In/Ga alloy paste. Noble metal and metal oxide deposited on Pt
board as H2 evolution co-catalyst were characterized and the photocatalytic activity of
which were evaluated. With the O2 evolution side architecture remained the same
(Au-NPs loaded SrTiO3), both the evolution yields of H2 and O2 were improved by all
kinds of co-catalysts deposited on the H2 evolution side. In this chapter, the performance
81
of H2 evolution was explored using noble metal such as Rhodium (Rh) and Ruthenium
(Ru) or their metal oxide as a co-catalyst in the plasmon-induced water splitting system,
among which the Rh showed the best enhancement as 3-fold. It is thus speculated that the
co-catalysts accelerated the electron transfer and its reaction with protons to form H2
evolution. The recombination of electrons and holes was reduced accordingly, resulted in
enhanced yields of both H2 and O2 evolution. Furthermore, the evaluation of various kinds
of co-catalysts with the effects of Schottky barrier excluded became realizable since the
successfully formation of the ohmic contact between the semiconductor material and the
H2 evolution co-catalyst. Moreover, H2 and O2 evolutions were performed in different
chambers with cathode and anode, respectively. Au-NPs side works as anode for O2
evolution and Pt board with metal or metal oxide co-catalyst side works cathode for H2
evolution. Therefore, O2 and H2 were evolved from the surface and the back of the same
SrTiO3 substrate according to separate the evolved H2 and O2 as the result. The separation
of H2 and O2 evolution in different chambers was supposed to inhibit the backward
reactions so as to enhance the water splitting efficiency. According to eliminate the
Schottky barrier effect and avoid a reverse reaction of water splitting, it becomes possible
to evaluate co-catalyst effects on H2 evolution.
82
3.3 Experimental details
3.3.1 Preparation of noble metal and metal oxide co-catalyst
Pt thin film was sputtered on the back side of the SrTiO3 using Super Fine Coater
ESC-101 (ELIONIX, Japan) with a deposition rate of 0.2 Å/s. The Ru and Rh species thin
films were deposited onto the Pt substrate (10 × 10 × 0.2 mm3, 99.98%, Nilaco
Corporation) by a co-sputtering system (ACS-4000-C3-HS, ULVAC Co.), and the distance
from the target to the substrate was maintained at 150 mm. The targets were ruthenium
and rhodium metal with a purity of 99.95%, respectively. For the Ru and Rh oxide thin
film deposition, a mixture of Ar and O2 flow was maintained during the sputtering process.
Whereas for the metallic Ru and Rh fabrication, an Ar gas flow with a rate of 29 sccm was
induced in the absence of O2 flow. The deposition pressure was kept at 2.9×10−1
Pa. The
substrate was without intentional heating during the deposition processes. The Pt board
with noble metal or metal oxide thin film on the surface was adhered to the backside of the
Nb-SrTiO3 substrate via Ag paste (D-550, Fujikura Kasei). The X-ray photoemission
spectrum (XPS) characterization was performed by X-ray photoemission spectrometer
(JPS-9200, JEOL, Japan). The center part with 3 mm × 3 mm area of the substrate surface
was used for XPS characterization. The AlKa line was used as the X-ray source. The C 1s
signal was used as an internal reference (284.6 eV). The cross sectional structure and the
elemental distribution of the thin films on the Pt board were analyzed by using
transmission electron microscopy (TEM) and energy dispersive X-ray spectroscopy (EDS)
on JEOL JEM-ARM 200F with aberration correction.
3.3.2 Electrochemical measurements
Bare Pt board and Pt boards with 2 nm Ru or Rh thin film prepared by the sputtering
process were used as the working electrodes. Ag paste (D-550, Fujikura Kasei) film was
pasted on the back of the Pt substrate and connected to the electrochemical analyzer
(ALS/CH Instruments 852C, ALS) with a lead wire. A platinum wire and a saturated
83
calomel electrode (SCE) were used as the counter electrode and reference electrode,
respectively. The electrochemical properties of the electrodes were measured in an
aqueous solution of 0.05 M K2SO4 adjusted to pH 1 with H2SO4 with continuous N2
bubbling.
84
3.4 Results and discussion
3.4.1 Elimination of the Schottky barrier effect
In this study, a 0.05 wt% niobium (Nb)-doped strontium titanate (Nb-SrTiO3) single
crystal with a bad gap of 3.2 eV was employed as a semiconductor photoelectrode for
efficient water splitting. The water splitting system comprises two reaction chambers
separated by the Au-NPs loaded Nb-SrTiO3 substrate, as shown in Figure 3.1. In order to
facilitate the water splitting reaction, a chemical bias was applied between the H2- and
O2-evolution chambers. Specifically, the pH was regulated using hydrochloric acid (HCl)
and potassium hydroxide (KOH) aqueous solutions with a concentration of both 0.1 M.
Hence, the pH value in the front side chamber (O2 evolution side) was regulated at 13
while that in the back side chamber (H2 evolution side) was set at 1 with alkaline and
acidic aqueous solutions, respectively. According to the Nernst equation, the relationship
between the redox potential (U0) and the pH value at 25ºC is given by:
U 0
= U 0
(pH = 0) − 0.059 × pH (3-1)
Therefore, the chemical bias applied between the two chambers was estimated to be 0.71
V.[14]
Figure 3.1 A schematic diagram illustrating the water splitting device using the
Au-NP-loaded Nb-SrTiO3 photoelectrode.
85
A φ6 mm2 area of the gold-nanostructured Nb-SrTiO3 substrate was irradiated by a
xenon lamp with a light intensity of 0.32 W/cm2 and a wavelength spectrally filtered from
550 nm to 650 nm as a visible light source in this experiment. The incident photon flux
was measured using spectroradiometer (MSR-7000N, Optoresearch Co.). Under the
irradiation of visible light to Au-NPs, plasmon-induced charge separation between
Au-NPs and Nb-SrTiO3, and subsequent water oxidation are supposed to take place at the
front side chamber, so as to promote the O2 evolution. Whereas in the back side chamber,
H2 evolution is expected on account of the reduction of protons by photogenerated
electrons injected into the conduction band of Nb-SrTiO3 at Pt surface used as a cathode
material. A conventional salt bridge with 2% of agar in weight ratio was employed to
maintain the charge balance between these compartments. It was clearly confirmed that
the pH value did not change before and after the irradiation in each experiment, the salt
bridge was thus verified to be effective.
Figure 3.2 A schematic illustration of the photoelectrode architecture for water splitting
using a Pt board (a) and a Pt thin film (b) as the hydrogen evolution site, and the
irradiation time dependence of H2 (solid circles) and O2 (open circles) evolution (c) by
86
which respectively. The red and blue colors correspond to the Pt board and Pt thin film,
respectively.
In order to demonstrate the effect of the Schottky barrier to the water splitting
activity in the present system, substrates with different cathode structure were fabricated.
Their architectures and the H2 and O2 evolution time dependence are shown in Figure 3.2
(a) and (b), respectively. For the contrastive structure, Pt thin film with a thickness of 1
nm was sputtered on the back side of the Nb-SrTiO3 substrate, as a substitute for the Pt
board.
From the separate experiment, it has been confirmed that water splitting efficiency
was best with a Pt thickness of 1 nm when Pt thin film was deposited by sputtering
directly on the SrTiO3 substrate. The averaged thickness of Pt film was controlled by
sputtering time and determined by an absolute calibration method. Therefore, the film
might be discontinuous because the film thickness was set to less than a grain size of 2 nm
in this Pt sputtering process.
The XPS spectra of the back side Nb-SrTiO3 surface before and after Pt nanoparticles
deposition are shown in Figure 3.3. Characterization of Pt nanoparticles was conducted by
X-ray photoemission spectrum (XPS, JPC-9010MC, JEOL). The AlKa line was used as
the X-ray source. The C 1s signal was used as an internal reference (284.6 eV).
Under the irradiated conditions, the evolution of H2 and O2 is linearly increased with
an irradiation time by both kinds of the structures. Stoichiometric evolution of H2 and O2
(2:1) was observed in both cases. Note that the H2 and O2 evolution by the photoelectrode
with Pt thin film are only half that of the one with Pt board stick on the Nb-SrTiO3 via
In/Ga alloy. Without Au-NPs decoration, it has been confirmed that neither H2 nor O2 was
evolved from a Nb-SrTiO3 substrate under the same irradiation conditions. No production
of H2 or O2 was observed by either photoelectrode architecture in the absence of
irradiation for up to 6 hours.
87
Figure 3.3 Partial XPS spectra of the Nb-SrTiO3 loaded with Pt nanoparticles. A
comparison of before and after the Pt nanoparticle deposition on the back side surface.
Figure 3.4 depicts the energy band alignment of the composite substrate structure. It
is hypothesized that an excited electron is transferred to the conduction band of SrTiO3
immediately following the inter- or intraband transition of the Au-NPs induced by the
plasmonically enhanced optical near-field or by hot electron transfer, thus leaving an
electron hole trapped at the surface states of the SrTiO3 near the Au/SrTiO3/water
interface. The trapped holes can subsequently induce the oxidation of hydroxyl ion or
water molecules efficiently via multi electron transfer.[15]
There is a potential gradient
between the two sides of the Nb-SrTiO3 substrate because a chemical bias was applied by
pH regulations. Under the influence of this potential gradient, the photogenerated
electrons injected into the conduction band of SrTiO3 transferred to the back side and
subsequently induced the reduction of proton at the Pt surface. With the Pt nanoparticles
on the back side of the Nb-SrTiO3, there is an undesired Schottky barrier between the
Nb-SrTiO3 and Pt, which hindered the electrons from transferring to the cathode, resulting
in the relatively lower H2 and O2 evolution efficiency. Whereas using In/Ga alloy to stick
the Pt board with the Nb-SrTiO3 substrate, an ohmic contact is very important for the H2
evolution in the plasmon-induced water splitting system, so as to facilitate the electron
transfer.
88
Figure 3.4 Energy band alignment of the plasmon-induced water splitting system with the
Au-NPs loaded SrTiO3 substrate using Pt nanoparticles (a) and a Pt board (b) as the
hydrogen evolution site respectively. UFB and U0 show the flat band potential of SrTiO3
and the redox potentials versus SHE (standard hydrogen electrode), respectively. The
symbols [−] and [+] indicate electrons and holes.
89
3.4.2 Characteristics of the Ru and Rh species thin film on Pt board
A water splitting system is commonly composed of a semiconductor material and
co-catalysts for H2 and O2 evolution, respectively. The photocatalytic activity of the
system is highly dependent on the co-catalysts and their properties. Hence, the evaluation
of different co-catalysts becomes a very important issue.[16, 17]
Based on the as mentioned
composite structure, the Schottky barrier between the co-catalyst and the semiconductor
could be eliminated, giving out the possibility to verify the performance of various kinds
of co-catalysts.
The ruthenium (Ru)[18, 19]
and rhodium (Rh)[20, 21]
species, which have been
considered to be excellent co-catalysts for H2 evolution, were employed in the present
study. A thin film of these two metals with a thickness of 2 or 3 nm was deposited by
sputtering on the Pt board and served as a co-catalyst for H2 evolution. By precisely
controlling the oxygen flow during the sputtering process, oxide of Ru and Rh species
were also prepared, respectively. The cross sectional view of a transmission electron
microscope (TEM) image of Rh thin film with a thickness of 3 nm deposited on the Pt
board by sputtering is shown in Figure 3.5(a) and its corresponding energy dispersive
X-ray spectrometry (EDS) image is shown in Figure 3.5(b). It was obviously confirmed
that a continuous Rh thin film with a thickness of 3 nm was formed on the Pt board
surface. On the other hand, the cross sectional view of TEM image of rhodium oxide with
a thickness of 4 nm and its corresponding EDS image are shown in Figure 3.5(c) and
3.5(d), respectively. Although images of the film with a thickness of 4 nm were
demonstrated here instead of 2 or 3 nm film for easier understanding by TEM observation,
importantly, rougher surface is clearly observed in the case of rhodium oxide film as
compared to the Rh film. The top view SEM images for Pt boards partially covered by
these thin films are shown in Figure 3.6. Due to the difference in the conductivity, all the
thin films show a relatively dark color compared with the bare Pt board.
90
Figure 3.5 Cross sectional view of transmission electron microscope images for (a) Rh, (c)
RhOx, (e) Ru and (g) RuOx, and their corresponding energy dispersive X-ray
spectrometry (EDS) images (b) Rh, (d) RhOx, (f) Ru and (h) RuOx thin films deposited on
the Pt board by sputtering. The signal of Rh/Ru and Pt in the EDS images is indicated by
green and blue colors, respectively. The scale bars represent 5 nm in the all images.
91
Figure 3.6 The scanning electron microscope images for (a) Ru, (b) RuOx, (c) Rh, and (d)
RhOx thin film deposited on the Pt board by compact sputtering. The scale bars represent
1 μm in the all images.
The XPS spectra of the metal and oxide of Ru and Rh are shown in Figure 3.7.
Without O2 flow during the sputtering process, the peak positions of the Ru species are at
461.3 and 483.5 eV for Ru 3p3/2 and 3p1/2, the peak positions of the Rh species are at 306.5
and 311.3 eV for Rh 3d5/2 and 3d3/2, which are all in good coincidence with the standard
values of the metallic species.[22]
Whereas with O2 flow during the sputtering process, the
as-deposited Ru and Rh species are clearly oxidized, but not as much as a RuO2 or Rh2O3
bulk reference. (462.7 and 484.8 eV correspond to the Ru4+
oxide RuO2, 308.4 and 313.2
eV correspond to the Rh3+
oxide Rh2O3). Accordingly, these oxides will be referred to as
RuOx and RhOx hereafter, respectively. Figure 3.8 depicts the thickness dependence of
partial XPS spectra for RuOx thin film deposited on the Pt board. With an increased RuOx
thickness, the corresponding XPS peak area ratio between Ru 3p and Pt 4f increase almost
linearly.
92
Figure 3.7 XPS spectra for (a) Ru 3p and (b) Rh 3d thin films sputtered with (red solid
line) and without (black solid line) O2 flow on the Pt board. The black and the red dashed
lines indicate the standard metal and oxidation state peak positions of Ru and Rh,
respectively.
Figure 3.8 (a) The thickness dependence of partial XPS spectra for RuOx thin film
deposited on the Pt board, the black, red, blue and green lines indicate the RuOx thickness
of 1, 2, 3 and 4 nm, respectively. (b) The corresponding XPS peak area ratio between Ru
3p and Pt 4f.
93
3.4.3 Water splitting performance using various H2 evolution co-catalyst
Water splitting was conducted with all kinds of the co-catalysts and with a bare Pt
board as a control experiment. The schematic illustration of the photoelectrode
architecture is shown in Figure 3.9(a). Figure 3.9(b) depicts the irradiation time
dependence of photocatalytic H2 and O2 evolution over 2 nm Rh on the Pt board.
Stoichiometric evolution of H2 and O2 (2:1) was still observed in the case of Rh
co-catalyst. This result indicated that noble metal deposited on Pt does not involve any
side reactions and works well as a co-catalyst for H2 evolution. Figure 3.9(b) also shows
the result of recycling reactions to verify the stability of the water splitting system.
Significantly, the reaction proceeded with no noticeable deactivation in the 4 rounds
recycling reactions with an irradiation time sums up to more than 80 h, demonstrating the
good stability of the present architecture. With the reaction time approached 6 hours, the
photocatalytic activity tends to be saturated. The increase of pressure due to the evolved
gas in the system seemed to suppress further evolution of H2 and O2. Hence, various kinds
of noble metal and metal oxide were used as H2 evolution co-catalyst for comparison and
the corresponding rates of H2 and O2 evolution is shown in Figure 3.9(c). The evolution of
both H2 and O2 is linearly increased with an irradiation time in all cases. The quantity of
H2 evolved from the surface of all kinds of reduction co-catalyst is twice that of O2
evolved from the Au nanostructured surface. Therefore, stoichiometric evolution of H2
and O2 was obviously demonstrated by various co-catalysts.
Compared with the bare Pt board, the H2 evolution rate has been enhanced by all
co-catalysts to varying degrees. These co-catalysts are supposed to facilitate the electron
transfer and its reaction with the protons in the acidic solution environment. The primary
role of the noble-metal or metal oxide thin film on the Pt board is to offer active sites for
H2 evolution reaction.[23]
Thus, all above-mentioned results indicate that the
Au-NPs/Nb-SrTiO3/In-Ga alloy/Pt/co-catalyst architecture is a promising candidate as
photocatalysts. Similar tendency was also observed using co-catalyst film with a thickness
of 3 nm.
94
Figure 3.9 (a) A schematic illustration of the photoelectrode architecture for the overall
water splitting using a Pt board decorated with various kinds of co-catalysts as the
hydrogen evolution site. (b) The recycling irradiation time dependence of H2 and O2
evolution by the present water splitting system using Rh deposited on the Pt board as the
H2 evolution co-catalyst with a thickness of 2 nm. (c) A comparison for the rates of H2
(pattern filled bars) and O2 evolution (open bars) by the water splitting system using a Pt
board decorated with various kinds of co-catalyst respectively.
The stability of the noble metal and metal oxide co-catalysts under visible light
irradiation was confirmed using XPS. Each of the Pt boards with co-catalysts after 24 h
light irradiation was collected and served for the measurements. Neither Ru 3p, Ru 3d, Rh
3p nor Rh 3d XPS spectra was changed after the irradiation by all kinds of the co-catalysts
(Figure 3.10). Therefore, the present noble metal or metal oxide on the Pt board was quite
stable under the present experimental conditions.
95
Figure 3.10 XPS spectra of Ru 3p and 3d for (a) Ru, (b) RuOx and Rh 3p and 3d for (c)
Rh, (d) RhOx thin film on the Pt board before (black) and after (red) water splitting
reaction for 24 h.
With the purpose of further confirming the function of the ohmic contact, as a
comparison, a RuOx thin film with a thickness of 2 nm used as the H2 evolution
co-catalyst was deposited directly on the back side of the Nb-SrTiO3 substrate in the
absence of the In/Ga alloy and Pt board. The composite substrate structure and the
corresponding time dependence of H2 and O2 evolution are shown in Figure 3.11. It was
confirmed that the water splitting yield markedly declined without the In/Ga alloy and Pt
board.
96
Figure 3.11 A schematic illustration of the photoelectrode architecture for water splitting
using RuOx thin film with a thickness of 2 nm deposited on the Pt board (a) and directly
on the Nb-SrTiO3 substrate (b) as the hydrogen evolution site, and the irradiation time
dependence of H2 (solid circles) and O2 (open circles) evolution (c) by which respectively.
The red and blue colors correspond to with and without the Pt board, respectively.
As have been reported by many researchers, some noble metals and metal oxides
deposited on a photocatalyst work as co-catalysts for H2 evolution even in this
plasmon-induced water splitting. Ideally, the reaction occurring on such co-catalysts
should be hydrogen evolution. In some cases, however, undesirable reverse reactions, such
as H2–O2 recombination to form H2O and photoreduction of O2, occasionally take place
on the surface of such co-catalysts, thereby hindering the forward reaction. To solve these
problems, Maeda et al. reported that using Cr2O3 shell, which is permeable to protons and
hydrogen but not oxygen, photodeposited on noble-metals or metal oxides to prevent the
reverse reactions.[24-26]
With the unique two chamber structure, the water splitting system
97
presented in this study is also capable to suppress the reverse reactions by the separate
evolution of H2 and O2. Furthermore, certain metal oxides, RuO2 for instance, can work as
both a water reduction and oxidation site during the water-splitting reaction.[27, 28]
The
separation of the H2 evolution co-catalyst from O2 evolution co-catalyst in two different
chambers with different solution environment provides a new approach to investigate
individual co-catalyst, excluding the influence from the other.
Cyclic voltammograms of the bare and Ru-, Rh-coated Pt electrodes obtained with
continuous N2 bubbling are shown in Figure 3.12. The currents indicating proton
adsorption/desorption and hydrogen evolution were observed at from -0.2 to -0.1 V and
-0.3 V, respectively, on all cases. For the Rh-coated Pt electrode, the current showed an
enhanced slope compared with the bare Pt board when the voltage tends to -0.3V,
indicating the H2 evolution had been kinetically accelerated by the Rh decoration.
However, the onset potential exhibited a negative shift with Rh thin film, revealing that it
is thermodynamically adverse to the proton reduction. Whereas in the case of the Ru
coating, on the contrary, the proton reduction and the H2 evolution had an advantage
thermodynamically, yet they suffered kinetically. Therefore, the higher yield of the H2
evolution obtained by the Rh as a co-catalyst is presumably ascribed to the interplay
between the above-mentioned two aspects. Furthermore, the work function of Rh (4.98 eV)
is higher than that of Ru (4.71 eV). The electron transfer from Pt (with a work function of
5.65 eV) to the H2 evolution co-catalyst might be thus preferable in case of Rh compared
with Ru. The same tendency has been reported previously.[29]
98
Figure 3.12 Cyclic voltammograms for bare and 2 nm Ru- and Rh-coated Pt electrodes in
0.05 M K2SO4 aqueous solution adjusted to pH 1 with H2SO4 under N2 bubbling (scan rate,
50 mV/s).
The relatively higher yield of the H2 evolution obtained by the Rh than the Ru as a
co-catalyst is presumably ascribed to the difference of the free energy of hydrogen
adsorption ∆GH. It was reported that this quantity is highly concerned with hydrogen
evolution activity for a wide variety of metals and alloys. Actually, it is reported that the
absolute value of ∆GH of Rh is lower than that of Ru from DFT calculations. This means
that the H2 evolution is preferable in the case of Rh co-catalysts as compared to Ru one.
As the result, rhodium thin layer with a thickness of 2 or 3 nm deposited on platinum
board exhibited relatively high performance as a 3-fold increment compared with the
absence of a metal or metal oxide co-catalyst thin layer. Furthermore, the co-catalyst
effects for H2 evolution in the plasmon-induced water splitting system have been
successfully evaluated according to eliminate the Schottky barrier effect and separate two
reaction chambers for hydrogen and oxygen evolutions to avoid a reverse reaction of
water splitting.
3.4.4 Dependence of co-catalyst thickness on water splitting activity
Among all the co-catalysts examined, Rh showed the highest yield. Therefore, Rh
was selected for the further investigation for the co-catalyst thickness dependence of the
H2 and O2 evolution efficiency. As depicted in Figure 3.13, stoichiometric evolution of H2
and O2 was clearly observed with Rh co-catalyst by all thicknesses. With the increment of
the Rh thickness, the rates of H2 and O2 evolution both increased up to 2 nm Rh thin film
thickness, beyond 3 nm they leveled off markedly and remained almost constant. A 3-fold
enhancement of the water splitting yield was obtained by the optimal Rh thickness,
compared with the absence of any co-catalyst. The relatively low H2 yield of the films
with a small quantity of Rh depositions is due to insufficient sites present to trap electrons.
99
On the other hand, the decrease in activity at higher Rh loadings is probably related to
excess coverage of the Rh nanoparticles deposited on the Pt board. Such excess loading
can cause an inner-filter effect, contributing to a decrease in activity.[30]
Figure 3.13 The rate of H2 and O2 evolution by the present water splitting system using
Rh thin film deposited on the Pt board as a H2 evolution co-catalyst with different
thickness.
100
3.5 Conclusions
In summary, a novel plasmon-induced water splitting system without an external
electrochemical apparatus was successfully developed. Using semiconductor single crystal
substrate to separate the two chambers for H2 and O2 evolution, the presented water
splitting system features a stable and simple architectural design. The separation of the
simultaneous evolution of H2 and O2 is supposed to suppress the recombination of the two
gases. The mechanism for the water splitting device is considered by plasmon-induced
charge separation at Au-NPs/SrTiO3 interface, thereby promoting water oxidation and
subsequent reduction of proton at the SrTiO3 backside. As a result of the field
enhancement by the LSPR near the Au-NPs, photoresponse has been expanded to the
visible region. In the present study, efforts have been focused on the co-catalyst effect on
H2 evolution in the plasmon-induced water splitting. A plasmon-induced water splitting
with noble-metal or metal oxide as a co-catalyst for H2 evolution without the Schottky
barrier effect and a reverse reaction of water splitting was successfully developed. The
Schottky barrier between the Pt cathode and the semiconductor material was successfully
removed by employing the In/Ga alloy paste. Thereupon, the accessible evaluation of
different kinds of co-catalysts would be possible due to the ohmic contact. With
noble-metal or metal oxide decorated on the Pt board as a H2 evolution co-catalyst,
stoichiometric evolution of H2 and O2 was observed in all cases, the yields of water
splitting has been enhanced to different levels. Among all the co-catalysts tested, metallic
Rh gives the greatest improvement of the efficiency as 3-fold compared with the absence
of any co-catalyst. The activity also shows a thickness dependence on the co-catalyst. In
addition, the plasmon-induced water splitting system with a noble metal as a co-catalyst is
highly stable with an irradiation time sums up to more than 80 h. It is of significance to
understand and to evaluate the roles of co-catalysts in photocatalytic reactions. The
present study has paved a new avenue of utilizing various co-catalysts in the design of
new and efficient systems for plasmon-induced water splitting.
101
3.6 References
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[12]. Liao, L. B., Zhang, Q. H., Su, Z. H., Zhao, Z. Z., Wang, Y. N., Li, Y., Lu, X. X., Wei, D. G., Feng, G.
Y., Yu, Q. K., Cai, X. J., Zhao, J. M., Ren, Z. F., Fang, H., Robles-Hernandez, F., Baldelli, S. and Bao, J. M.,
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[14]. Zaban, A., Ferrere, S., Sprague, J. and Gregg, B. A., pH-Dependent Redox Potential Induced in a
Sensitizing Dye by Adsorption onto TiO2. The Journal of Physical Chemistry B 1997, 101 (1), 55-57.
[15]. Thomann, I., Pinaud, B. A., Chen, Z. B., Clemens, B. M., Jaramillo, T. F. and Brongersma, M. L.,
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L., Kanehara, M., Setoyama, T., Teranishi, T. and Domen, K., Photocatalytic Overall Water Splitting
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[17]. Yang, J., Wang, D., Han, H. and Li, C., Roles of Cocatalysts in Photocatalysis and
Photoelectrocatalysis. Accounts of Chemical Research 2013, 46 (8), 1900-1909.
[18]. Sato, J., Saito, N., Yamada, Y., Maeda, K., Takata, T., Kondo, J. N., Hara, M., Kobayashi, H., Domen,
K. and Inoue, Y., RuO2-Loaded β-Ge3N4 as a Non-Oxide Photocatalyst for Overall Water Splitting. Journal
of The American Chemical Society 2005, 127 (12), 4150-4151.
[19]. Liu, H., Yuan, J., Shangguan, W. and Teraoka, Y., Visible-Light-Responding BiYWO6 Solid Solution
for Stoichiometric Photocatalytic Water Splitting. The Journal of Physical Chemistry C 2008, 112 (23),
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[20]. Hata, H., Kobayashi, Y., Bojan, V., Youngblood, W. J. and Mallouk, T. E., Direct Deposition of
Trivalent Rhodium Hydroxide Nanoparticles onto a Semiconducting Layered Calcium Niobate for
Photocatalytic Hydrogen Evolution. Nano letters 2008, 8 (3), 794-799.
[21]. Maeda, K., Masuda, H. and Domen, K., Effect of electrolyte addition on activity of (Ga1−xZnx)(N1−xOx)
photocatalyst for overall water splitting under visible light. Catalysis Today 2009, 147 (3–4), 173-178.
[22]. Kezilebieke, S., Ali, M., Shadeke, B. and Gunnella, R., Magnetic properties of ultrathin Ni81Fe19 films
with Ta and Ru capping layers. Journal of Physics-condensed Matter 2013, 25 (47), 476003.
[23]. Maeda, K., Lu, D. and Domen, K., Direct Water Splitting into Hydrogen and Oxygen under Visible
103
Light by using Modified TaON Photocatalysts with d0 Electronic Configuration. Chemistry – A European
Journal 2013, 19 (16), 4986-4991.
[24]. Sakamoto, N., Ohtsuka, H., Ikeda, T., Maeda, K., Lu, D., Kanehara, M., Teramura, K., Teranishi, T.
and Domen, K., Highly dispersed noble-metal/chromia (core/shell) nanoparticles as efficient hydrogen
evolution promoters for photocatalytic overall water splitting under visible light. Nanoscale 2009, 1 (1),
106-109.
[25]. Maeda, K., Sakamoto, N., Ikeda, T., Ohtsuka, H., Xiong, A., Lu, D., Kanehara, M., Teranishi, T. and
Domen, K., Preparation of Core–Shell-Structured Nanoparticles (with a Noble-Metal or Metal Oxide Core
and a Chromia Shell) and Their Application in Water Splitting by Means of Visible Light. Chemistry – A
European Journal 2010, 16 (26), 7750-7759.
[26]. Yoshida, M., Takanabe, K., Maeda, K., Ishikawa, A., Kubota, J., Sakata, Y., Ikezawa, Y. and Domen,
K., Role and Function of Noble-Metal/Cr-Layer Core/Shell Structure Cocatalysts for Photocatalytic Overall
Water Splitting Studied by Model Electrodes. The Journal of Physical Chemistry C 2009, 113 (23),
10151-10157.
[27]. Lee, Y., Teramura, K., Hara, M. and Domen, K., Modification of (Zn1+xGe)(N2Ox) Solid Solution as a
Visible Light Driven Photocatalyst for Overall Water Splitting. Chemistry Of Materials 2007, 19 (8),
2120-2127.
[28]. Maeda, K., Abe, R. and Domen, K., Role and Function of Ruthenium Species as Promoters with
TaON-Based Photocatalysts for Oxygen Evolution in Two-Step Water Splitting under Visible Light. The
Journal of Physical Chemistry C 2011, 115 (7), 3057-3064.
[29]. Kitano, M., Tsujimaru, K. and Anpo, M., Decomposition of water in the separate evolution of
hydrogen and oxygen using visible light-responsive TiO2 thin film photocatalysts: Effect of the work
function of the substrates on the yield of the reaction. Applied Catalysis A-general 2006, 314 (2), 179-183.
[30]. Bao, N., Shen, L., Takata, T. and Domen, K., Self-Templated Synthesis of Nanoporous CdS
Nanostructures for Highly Efficient Photocatalytic Hydrogen Production under Visible Light. Chemistry of
Materials 2007, 20 (1), 110-117.
104
Chapter 4
Plasmon-Induced Water Splitting Utilizing Heterojunction
Synergistic Effect between SrTiO3 and Rutile TiO2
4.1 Abstract
A facile plasmon-enhanced water splitting system using gold nanostructured
strontium titanate (SrTiO3) single crystal photoelectrode with titanium dioxide (TiO2) thin
film heterojunction was developed. Simultaneous evolution of hydrogen (H2) and oxygen
(O2) in stoichiometric ratio was successfully observed in separate reaction chambers under
visible light irradiation. The substrate composed of single crystal SrTiO3 with the rutile
TiO2 thin film heterojunction exhibited enhanced water spitting activity compared with the
absence of TiO2 thin film because the back electron transfer reaction might be prevented
due to the synergistic effect. A thickness dependence of the Pt co-catalyst on the water
splitting activity is also discussed.
105
4.2 Introduction
The human demand for energy is increasing dramatically in recent years, while the
fossil fuel is diminishing and may exhaust in the next few decades. Moreover, we have
long been puzzled by environment problems caused by the usage of fossil fuel, e.g.
greenhouse gas emissions. Therefore, it is crucial to exploit a new energy source to replace
the traditional one. Among all the novel energy considered and explored, solar energy
draws much attention since it is clean, abundant, widespread, and inexhaustible. Because
fuel cells can convert hydrogen to electrical energy with high efficiency, hydrogen serves
as an important chemical energy storage material. The use of hydrogen has been restricted
to industrial applications until now, it is currently being expanded for use as a new energy
source.
The construction of a light-energy conversion system that uses sunlight for
renewable energy with high efficiency is required for the realization of a low-carbon
society. Artificial photosynthesis, which stores solar energy as a stable chemical and
enables energy use when required, is an important subject. It has attracted attention as a
method for storing useful chemical energy, as the form of hydrogen, without any
environmental impact. Because the required components for hydrogen generation are only
water and sunlight, these energy storage products can be generated using reactants that are
virtually infinitely available on Earth. The construction of an artificial photosynthesis
system that is sensitive to light energy from ultraviolet to near-infrared wavelengths is
indispensable for enhancing the solar energy conversion efficiency of artificial
photosynthesis.
H2 evolution via a photoelectrochemical water splitting using solar light irradiation
has been extensively studied ever since the pioneering investigation of Honda and
Fujishima in 1971.[1, 2]
Since then, water splitting systems that respond to visible light
have been developed according to doping the semiconductor materials with metal ion,[3, 4]
utilizing a Z-scheme process with a combination of two kinds of visible wavelength
semiconductors via redox mediator,[5]
and using dye or plasmon sensitization.[6]
106
A plasmon-assisted water splitting system using two sides of the same SrTiO3
single crystal substrate with Au-NPs on the front side and a platinum (Pt) board with
ohmic contact on the back side was successfully demonstrated in the previous chapter. In
this system, it is considered that an excited electron is transferred to the conduction band
of SrTiO3 following the inter- or intraband transition of the Au-NPs induced by the
plasmonically enhanced optical near-field. Thus the electron migrates to the back side of
the SrTiO3 substrate and reduces protons on the Pt co-catalyst surface for H2 evolution. On
the other hand, a hole in the Au-NPs might be trapped on the surface state of the SrTiO3
near the Au/SrTiO3/water interface, and the trapped holes can subsequently induce the
oxidation of hydroxyl ions or water molecules efficiently via multi electron transfer for O2
evolution.[7]
On despite of the progress made in recent few years, the relatively low efficiency
still hinders the application of the plasmon-assisted water splitting system. One of the
conventional problems lies in the rapid recombination between electron and hole after the
charge separation. The unidirectional transportation of electrons utilizing two types of
semiconductors with different conduction band energies is thus preferable for use in
photoelectrochemical water splitting systems so as to prevent the backward electron
transfer.
It is known that a mixture of anatase/rutile TiO2 materials have been reported to
exhibit advanced performance for photocatalytic reactions.[8-11]
It is considered that the
mechanism was ascribed to the different energy band structures between anatase and rutile
TiO2. It is commonly known that SrTiO3 shares similar energy band structure with anatase
TiO2.[12]
Hence, it is of significance to elucidate the synergistic effect of the combination
of SrTiO3 and rutile or anatase TiO2 on the plasmon-induced water splitting system. In this
chapter, an improvement of plasmon-enhanced water splitting using Au-NPs loaded
SrTiO3 single crystal photoelectrode with a TiO2 thin film heterojunction is explored. The
H2 evolution co-catalyst thickness dependence of the water splitting yields is investigated.
The role of semiconductor materials with different energy band structure is also discussed.
107
4.3 Experimental details
Single-crystal strontium titanate (SrTiO3, 0.05wt% niobium doped, 10 × 10 × 0.5
mm3, Furuuchi Chemical Co.) with a (110) surface was used as a semiconductor substrate
for water splitting in this study. A thin gold film with a thickness of 3 nm was deposited
onto the front side of the SrTiO3 by helicon sputtering (MPS-4000, ULVAC Co.) at a
deposition rate of 1 Å/s. The substrate was subsequently annealed at a temperature of
800°C for 1 h in a nitrogen atmosphere. The thin film was transformed to discontinuous
gold nanoparticles (Au-NPs) after annealing. On the other hand, as a H2 evolution
co-catalyst, a Pt thin film was subsequently sputtered by an ESC-101 Super Fine Coater
(ELIONIX Co.) on the back side of the SrTiO3 substrate.
4.3.1 Preparation and characterization of the TiO2 thin film
Atomic layer deposition (ALD) is a method for depositing thin films conformally on
substrates with uniform thickness. It is a self-limiting process in which the film thickness
can be accurately controlled by reaction cycles. (Figure 4.1 shows a reaction cycle for a
layer of TiO2 growth.) The low deposition temperature and purging procedure make ALD
advantageous in preventing substrates from other unnecessary side reactions. It is
therefore very useful for growing oxides (e.g. TiO2 and Al2O3), nitrides (e.g. TiN and TaN),
and high-k dielectrics for electronic applications. This method was adopted to grow
heterojunction nanomaterials and fabricate electronic devices.
Titanium dioxide thin films with different thicknesses were deposited onto the
SrTiO3 substrate using a commercial hot-wall flow-type ALD reactor (SUNALETM R
series Atomic Layer Deposition reactors, Picosun, Espoo, Finland). The deposition
procedure involved alternating exposure of TiCl4 and deionized water vapor at a process
temperature of 300 °C with N2 as a precursor carrier and purge gas at a pressure of 1.6 kPa.
The pulse and purge times for the precursors were 0.1 and 4 s, respectively. The
deposition rate of TiO2 on the SrTiO3 substrate was estimated to be 0.41 Å per cycle. To
108
fabricate uniform, one sided deposition TiO2 films, the SrTiO3 substrate was tightly
attached to a smooth cover glass, which was washed with deionized water in an ultrasonic
bath for 5 min. The TiO2 film thickness was estimated from the interference oscillations in
the visible spectra using an optical spectroscopic reflectometer (F20, Filmetrics, U.S.A.)
with a lower bound accuracy of ±2 nm, and the difference between film thicknesses is ±4
nm.
The reaction process is
1. (-OH) (s) + TiCl4 (g) → (-O-)TiCl3 (s) + HCl (g) (adsorption) (4-1)
2. (-O-)TiCl3 (s) + 2H2O (g) → (-O-)TiO(OH) (s) + 3HCl (g) (reaction) (4-2)
Figure 4.1 Reaction cycle for the growth of one layer of TiO2 on the SrTiO3 substrate by
atomic layer deposition.
The X-ray diffraction spectra of the TiO2 thin films were recorded with a RIGAKU
RINT-2000/PC using Cu Kα radiation and a scanning speed of 2° (2θ)/min within the 2θ
range from 20 to 80°. Characterization of the TiO2 thin film was also conducted by X-ray
photoemission spectrum (XPS, JPC-9010MC, JEOL). The AlKa line was used as the
X-ray source. The C 1s signal was used as an internal reference (284.6 eV).
109
4.4 Results and discussion
4.4.1 Dependence of Pt co-catalyst thickness on water splitting activity
The plasmon-induced water splitting system was constructed as a sealed reaction cell
with two chambers, which were separated by the SrTiO3 substrate as shown in Figure
4.2.[7, 13]
The Au-NPs decorated surface was on the front side, which was irradiated by
visible light, whereas the surface with Pt thin film was on the back side. The pH values for
the front and back side chambers were adjusted to 13 and 1 using aqueous potassium
hydroxide (KOH) and hydrochloric acid (HCl) solutions respectively. These two reactions
were supposed to take place in the front and back side respectively:
4h++4OH
- → O2 + 2H2O (4-3)
2e- + 2H
+ → H2 (4-4)
The acidic and alkaline conditions were engaged as a chemical driving force to
promote these two reactions.[14-17]
To maintain the charge balance between the two
chambers, a conventional salt bridge with 2wt% agar was employed. The pH values for
both chambers were confirmed to be unchanged before and after each irradiation
experiment.
Figure 4.2 (a) A schematic illustration of a plasmon-induced water splitting system using
an Au-NPs loaded SrTiO3 substrate with a rutile TiO2 layer.
110
As shown in Figure 4.3, plasmonically-enhanced optical near-field promotes a hot
electron transfer from Au-NPs to the conduction band of SrTiO3, and namely
plasmon-induced charge separation is induced as the result.[18, 19]
The Pt on the back side
of the SrTiO3 is supposed to act as an electron trap site and co-catalyst for the H2 evolution.
The holes remaining in the Au-NPs, which might be trapped in the surface states of SrTiO3
near the Au/SrTiO3/water interface, induce the oxidation of water molecules and hydroxyl
ions to evolve O2.[20, 21]
According to the extinction spectrum of the Au-NPs on the SrTiO3 substrate, which
clearly show a localized surface plasmon resonance band. The samples were irradiated by
a xenon light spectrally filtered over the wavelength range of 550 nm to 650 nm with an
intensity of 0.32 W/cm2.
Figure 4.3 Energy band diagram of the plasmon-induced water splitting system using an
Au-NPs loaded SrTiO3 substrate with and without the rutile TiO2 layer. The symbols [−]
and [+] indicate electrons and holes, respectively.
First of all, the effect on the H2 evolution efficiency of the thickness of the Pt
co-catalyst film was explored in the plasmon-induced water splitting system. Samples
111
with different Pt thickness were fabricated, and their performance of the water splitting
was evaluated.
In this experiment, the average thickness of the Pt film was controlled by sputtering
time and was determined by an absolute calibration method. Therefore, there is a
possibility that the film may become discontinuous if the film thickness was set to less
than the grain size in Pt sputtering.[22]
Figure 4.4(a) depicts the irradiation time
dependence of the H2 and O2 evolution by the water splitting system with a Pt thickness
of 1 nm as a typical example. The evolution of both H2 and O2 increased almost linearly
with the extended irradiation time. Furthermore, the amount of evolved H2 was
approximately twice that of the evolved O2, demonstrating a stoichiometric ratio from
successful overall water splitting in all Pt thickness cases. In a separate experiment, it
was confirmed that neither H2 nor O2 was evolved from a SrTiO3 substrate without
Au-NPs under the same irradiation conditions. No production of H2 or O2 was observed
in the absence of irradiation over an extended period as long as 6 h, even with the
Au-NPs loaded on the SrTiO3 substrates. The water splitting activity by various Pt
co-catalyst loading amount, represented by the H2 evolution rates, is summarized in
Figure 4.4(b). The samples with Pt co-catalyst decoration all exhibited superior water
splitting performance compared with that in the absence of any co-catalyst. The activity
increased with Pt loading to a maximum at a thickness of 1 nm, above which the activity
decreased. The relatively lower H2 evolution efficiency with less Pt depositions is
considered to be attributed to the lower density of Pt particle grains based on the
insufficient sites for electron trapping because that the grain size in Pt sputtering is
estimated to be ∼2 nm using this apparatus, and a significantly thinner film is expected to
be discontinuous. While on the other hand, with increased Pt depositions, the active
surface sites and the surface area of the Pt will also decrease because the film gradually
becomes continuous, and hence resulted in lower water splitting performance. The Pt thin
film thickness was thus fixed as 1 nm in the following experiments.
112
Figure 4.4 (a) The irradiation time dependence of H2 and O2 evolution by the water
splitting system with a Pt co-catalyst thickness of 1 nm. (b) The Pt co-catalyst thickness
dependence of the H2 evolution rate.
The function of the Pt co-catalyst is speculated to be twofold. Firstly, it is capable to
trap the electrons transferred from the semiconductor substrate. The recombination
between electrons and holes is thus retarded. Secondly, the following three reactions are
supposed to take place in sequence during the H2 evolution process at the back side
chamber of the water splitting system:
Volmer reaction: e- + H
+ + Pt → Pt-H (4-5)
Heyrovsky reaction: e- + H
+ + Pt-H → H2 + Pt (4-6)
Tafel reaction: Pt-H + Pt-H → H2 + 2Pt (4-7)
The Pt-H represents the hydrogen atoms adsorbed on the Pt surface. The Volmer
reaction, the initial discharge of protons to give adsorbed hydrogen atom, is followed by
combination of an adsorbed hydrogen atom with a proton in the solution and an electron
to give H2 (Heyrovsky reaction) or the combination of two adsorbed hydrogen atoms
(Tafel reaction). Generally, with Pt as the cathode material, Tafel reaction would be the
rate determining step on account of its very small overpotential for the H2 evolution.
Whereas in the present study, it has been demonstrated that the proton concentration
greatly affects the H2 evolution. Detailed investigation is currently in process.
113
The Pt thin film works as a catalyst providing reaction site for the electrons and
protons to generate hydrogen radicals. Instead of diffusing into the solution, these
hydrogen radicals adsorbed at the surface of the Pt co-catalyst. Subsequently, two
hydrogen radicals combined and formed one hydrogen molecule evolution. Normally, the
backward reaction of the hydrogen radical formation would also occur. However, the
presence of the Pt functioned as a catalytic center effectively hindering this backward
reaction.
4.4.2 Characteristics of the TiO2 thin film
A TiO2 thin film with a thickness of 300 nm was deposited on the back side of a
SrTiO3 substrate by atomic layer deposition (SUNALETM R series, Picosun Oy.) prior to
the Pt decoration. The samples were subsequently annealed at different temperatures for 1
hour. The XRD investigation, as shown in Figure 4.5, indicates that the crystallographic
phase of the TiO2 thin film is anatase-type after annealing at 800°C, whereas it
transformed to rutile-type by increasing the annealing temperature to 1000°C.[23-26]
Figure 4.5 X-ray diffraction patterns of bare SrTiO3 (black line) and SrTiO3 substrates
with a TiO2 thin film annealed at 800°C (red line) and 1000°C (blue line), respectively.
114
Red letters and blue letters indicate facets derived from anatase and rutile TiO2,
respectively.
The surface element composition and chemical state of the sample were further
confirmed by XPS results, and the corresponding experimental results are shown in Figure
4.6. The Ti 2p XPS spectrum of the TiO2 thin film on the SrTiO3 substrate shows two
major peaks with binding energies at 464.9 eV and 459.1 eV, corresponding to Ti 2p3/2
and Ti 2p1/2, respectively, which are the typical characteristic of a TiO2 phase. The
spectrum of O 1s of the TiO2 thin film on the SrTiO3 substrate is observed with a peak at
binding energy located at 530.4 eV. This energy peak corresponds to the coordination of
oxygen in Ti–O–Ti. Furthermore, the Sr 3d peaks were detected only on the surface of
bare SrTiO3 substrate in the absence of the TiO2 deposition. Therefore, the thin film
fabricated by atomic layer deposition on the SrTiO3 substrate was thus confirmed to be
TiO2.
115
Figure 4.6 XPS survey spectra of SrTiO3 substrate with and without the TiO2 thin film by
atomic layer deposition: (a) Ti 2p, (b) O 1s, (c) Sr 3d.
4.4.3 Water splitting performance by TiO2 with different crystalline phases
Figure 4.7(a) demonstrates the H2 and O2 evolution rates of water splitting systems
with anatase or rutile TiO2 layers were comparable to that without any TiO2 layer between
the SrTiO3 substrate and the Pt co-catalyst. The activity was increased with rutile layer
decoration. The enhancement of the water spitting activity using a rutile-TiO2 layer is
estimated to be 25%. This might be due to the conduction band of rutile, which is 0.2 eV
lower than that of SrTiO3. As illustrated in Figure 4.3, because of the pH difference, there
is a potential gradient between the O2 evolution and H2 evolution sides of the substrate,
under the influence of which the excited electrons are transferred from the Au-NPs to the
Pt co-catalyst, so as to accomplish the water splitting reaction. With the lower conduction
band position at the H2 evolution side, the electron transfer is supposed to be further
facilitated due to the greater conduction band slope as result in the prevention of back
electron transfer, despite H2 evolution being thermodynamically disfavored by the forming
of the rutile TiO2 layer.
On the other hand, in the case of the water splitting system with the TiO2 as
anatase-type, whose conduction band energy is almost same as that of SrTiO3, the activity
decreased compared to that without the TiO2 layer. The reason is speculated to be that the
recombination between electron and hole is aggravated in this anatase layer, on account of
the inevitable formation of the lattice defects during the atomic layer deposition process.
These defects could serve as a recombination center for electrons and holes.[27]
It is
noteworthy that in all cases of the composite substrate architectures described above for
water splitting, the front side where the oxidation reaction took place for O2 evolution
remained unchanged, i.e., Au-NPs/SrTiO3. However, the activities varied remarkably, with
H2 and O2 evolution maintaining a stoichiometric ratio, as the semiconductor material or
116
the morphology of the H2 evolution co-catalyst changed. These aspects are thus
considered to play a key role in the water splitting reaction.
In addition, the water splitting experiment using the present system with a pH
combination of 9 and 1 in the front and back chambers was explored. The H2 and O2
evolution rates are shown in the following Figure 4.7(b). With a reduced chemical bias as
compared to that with a pH combination of 13 and 1, the water splitting activities
decreased in all cases with a stoichiometric ratio between H2 and O2 evolution maintained.
However, the enhancement of the water spitting activity using a rutile-TiO2 under layer
with a pH combination of 9 and 1 is estimated to be 56 %, remarkably higher than that
with a pH combination of 13 and 1 (25 %). This result supports the speculated mechanism
that the rutile-TiO2 under layer enhances a charge separation by forming larger energy
band bending. Whereas the water spitting activity using the TiO2 under layer as
anatase-type with a lower chemical bias is further decreased compared with that without
any TiO2 layer between the SrTiO3 substrate and the Pt co-catalyst.
Figure 4.7 H2 and O2 evolution rates of water splitting systems with anatase or rutile
layers compared with that without a TiO2 layer. The pH value in the H2 evolution side is
fixed at 1. The pH value in the O2 evolution side is fixed at 13 (a) and 9 (b) respectively.
The pattern filled bars and open bars in the graph indicate the rate of H2 and O2 evolutions,
respectively.
117
The lattice constant of the anatase TiO2 is rather closer to that of the SrTiO3 than the
rutile TiO2. In the case of the thin film deposition on the single crystal SrTiO3 surface, it
has been reported that the anatase TiO2 is preferred to be formed as compared to the rutile
TiO2.[28]
The transition temperature of TiO2 thin film from anatase to rutile phase is as
high as 1000℃ in this experiment, indicating the good stability of the anatase TiO2 on
SrTiO3 compared with the rutile TiO2. Thus, from the view point of the crystallinity, the
water spitting activity of the system with an anatase TiO2 under layer should be better than
that with a rutile TiO2 under layer. However, in despite of these considerations, the rutile
TiO2 under layer showed superior water spitting activity based on our experiment results.
This enhanced water spitting activity is thus speculated to be ascribed to the enhanced
charge separation by forming larger energy band bending with the rutile-TiO2 under layer.
118
4.5 Conclusions
In summary, an almost stoichiometric evolution of H2 and O2 at separate sites have
been successfully demonstrated by decorating noble metal nanoparticles and thin films on
the two sides of the same single crystal SrTiO3 substrate. The quantity of the evolved H2
and O2 increased linearly with the irradiation time. The activity of the water splitting was
found to be highly dependent on the loading amount of the Pt, which was used as a H2
evolution co-catalyst. The optimal thickness of the Pt thin film was determined to be 1 nm.
The electron transfer from the oxidation reaction site to the reduction reaction site was
facilitated by the synergistic effect of SrTiO3 and rutile TiO2, due to the difference
between their energy band structures. The water splitting efficiency was thus enhanced to
a certain degree.
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Chapter 5
Summary and Future Perspectives
5.1 Summary
Energy is at the heart of most critical economic, environmental and
developmental issues facing the world today. Clean, efficient, affordable and reliable
energy services are indispensable for global prosperity. This thesis describes our
efforts to develop a plasmon-assisted water splitting system under visible light
irradiation using gold nanostructured strontium titanate single crystals so as to address
the energy issues. This work defines a potential route for constructing efficient
composite photoelectrodes comprising a semiconductor substrate, a nanostructured
photo-sensitizer and a noble metal co-catalyst functioned for H2 evolution.
A novel water splitting system using two sides of the same SrTiO3 single crystal
substrate was designed and fabricated. The experimental apparatus has two reaction
chambers, separating the evolution of the H2 and O2. Numerical simulations indicated
that a plasmonic near field enhancement was formed at the interface between the
Au-NPs and the SrTiO3 single crystal substrates. Under the influence of this near field
enhancement, the optical absorption of the substrate was extended from UV light to
visible light region with a peak at 600 nm. In this water splitting system, unlike the
conventional ones, the reaction proceeded without any external electric bias. A
chemical bias formed by aqueous solutions with different pH values between the front
and back side of the composite photoelectrode was involved as a substitution. By
analyzing the action spectrum, the water splitting yields were found to be in good
consistent with the segmented integral area of the extinction spectrum of the Au-NPs.
H2 evolution from the water splitting is thus verified to be caused by the absorption of
the visible light. The pH value dependence of the water splitting activity was
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systematically investigated. It has been discovered that the efficient water oxidation
due to the plasmon effect reduced the minimum chemical bias that capable of driving
the visible-light response water splitting reaction to 0.23 V, which is the smallest
value ever reported so far. In addition, the stability of this water splitting system was
verified to be longer than 48 hours.
Based on the rational design of this reaction apparatus, the appropriate H2
evolution co-catalyst was explored in order to further increase the water splitting
activity. The schottky barrier was eliminated by using In/Ga alloy between the SrTiO3
substrate and the Pt board. Various noble metal and metal oxide thin film were
deposited on the Pt board as a H2 evolution co-catalyst, among which the metallic Rh
exhibited highest water splitting efficiency enhancement as 3 fold.
Besides the chemical bias regulation, semiconductor energy band engineering
was also taken into account in this thesis. Specifically, TiO2 thin films were deposited
on the SrTiO3 substrates as anatase and rutile crystal type by calcining in different
temperatures. The composite substrate with a rutile TiO2 under layer exhibited higher
H2 and O2 evolution rates because of its conduction band position difference with that
of the SrTiO3. The electron transfer through the substrate was thus facilitated and the
recombination between electrons and holes was hindered. Moreover, the size and
shape of the Pt, which was used as a H2 evolution co-catalyst, had a strong impact on
the activity of the water splitting reaction. The optimal thickness of the Pt thin film
was determined to be 1 nm.
In conclusion, it has been demonstrated in this thesis that a facile artificial
photosynthesis reaction system utilizing solar irradiation was successfully developed.
It is anticipated that the study presented here introduces new possibilities for efficient
and stable water splitting catalytic systems for clean fuel generation leading towards a
greener energy technology and sustainable future.
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5.2 Future Perspectives
On the basis of the results obtained in present study, the plasmon-enhanced water
splitting has been successfully demonstrated using solar light irradiation by Au-NPs
loaded strontium titanate single crystal substrates. The innovative design of the water
splitting system with only one substrate separating the H2 and O2 evolution sites
features some unique properties. However, the performances of these composite
photoelectrodes are still poor, and the active area for the solar light harvesting is
restricted to a very small range in the current stage. The present reaction system is
thus far away for large-scale production of water splitting. For the purpose of
large-scale application, several aspects should be considered.
The future outlook of this thesis study can be extended to:
(1) The water splitting reaction mechanism and interaction of the loaded co-catalyst
with the base semiconductor material is still not completely understood. A better
knowledge of this system is of course very useful in designing active photocatalysis
systems. Some attempts to investigate the mechanistic aspect on water splitting and
the co-catalyst/semiconductor interface by means of kinetic analysis, spectroscopic
and photoelectrochemical measurements, and computational approach have been
reported so far. Specifically, understanding the interfacial property between a
photocatalyst and the loaded cocatalyst would be the major challenge in this research
field.
(2) The extinction properties of the Au-NPs have already found to be highly
dependent on their size and shape. In the present study, visible irradiation with a
wavelength at ca. 600 nm was employed as a light source according to the extinction
spectrum. By varying the experimental conditions during the gold sputtering and
annealing process or using electron beam lithography technique to fabricate gold
nanostructure, an extended absorption to the longer wavelength (even in the infrared
region) could be expected. Solar energy conversion efficiency will be greatly
enhanced if we can make use of major part of the solar spectrum.
(3) In despite of the fact that the SrTiO3 substrate adopted in this study was single
125
crystal type, defects are inevitable with such a thickness. Recombination between
electrons and holes are likely to occur at these defects, the water splitting efficiency
would be suffered as a result. Therefore, thinner substrates are considered to be better
for avoiding losses due to electron trapping in the defect level. Furthermore, as a
substitution of the single crystal substrate, semiconductor thin films are recommended
to fabricate by atomic layer deposition or pulse laser deposition etc. so as to facilitate
the electron transfer.
(4) A practical evaluation method of the capability of co-catalyst has been presented
in this study. However, at the current status of the research, there are just a couple of
noble metal and metal oxides examined. Having a lot more co-catalyst materials
evaluated and finally constructing a co-catalyst library is of great guiding significance
for the artificial photosynthesis system design.
(5) While making hydrogen from water is important, it is not the only future target.
With the gold nanostructure as a light harvesting antenna, the present reaction system
is capable of charge separation and electron transportation driven by visible
irradiation. Multiple artificial photosynthesis reactions can be realized in the back side
chamber of the system. For instance, CO2 reduction into useful products and low
carbon fuels like methanol and formic acid, ammonia production by nitrogen gas
fixation, degradation of organic pollutants.
If these proposed goals are achieved, the present system could potentially be
used in constructing efficient and robust artificial photosynthesis systems that respond,
with lower chemical biases, to visible and near-infrared light.
The author believes that the present results are expected to give important
information for this research fields. Finally, the author would like to expect this
research field to be progressed more in the future.
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List of Publications
1. Y. Zhong, K. Ueno, Y. Mori, X. Shi, T. Oshikiri, K. Murakoshi, H. Inoue, H.
Misawa
“Plasmon-Assisted Water Splitting Using Two Sides of the Same SrTiO3
Single-Crystal Substrate: Conversion of Visible Light to Chemical Energy”
Angew. Chem. Int. Ed., 2014, 53, 10350-10354.
2. Y. Zhong, K. Ueno, Y. Mori, T. Oshikiri, H. Misawa
“Co-catalyst Effects on Hydrogen Evolution in a Plasmon-Induced Water
Splitting System”
J. Phys. Chem. C, 2015, 119, 8889-8897.
3. Y. Zhong, K. Ueno, Y. Mori, T. Oshikiri, H. Misawa
“Plasmon-Enhanced Water Splitting Utilizing the Heterojunction Synergistic
Effect between SrTiO3 and Rutile-TiO2”
Chem. Lett., 2015, 44, 618-620.
4. K. Ueno, T. Oshikiri, X. Shi, Y. Zhong, H. Misawa
“Plasmon-Induced Artificial Photosynthesis”
Interface Focus, 2015, 5, DOI: 10.1098/rsfs.2014.0082.