Applied Catalysis B: Environmental 176 (2015) 396–428
Contents lists available at ScienceDirect
Applied Catalysis B: Environmental
journal homepage: www.elsevier.com/locate/apcatb
Review
Self-cleaning applications of TiO2 by photo-induced hydrophilicity
and photocatalysis
Swagata Banerjee a , Dionysios D. Dionysiou b , Suresh C. Pillai c,d,∗
a
Centre for Research in Engineering Surface Technology (CREST), FOCAS Institute, Dublin Institute of Technology, Kevin St, Dublin 8, Ireland
Environmental Engineering and Science Program, Department of Biomedical, Chemical and Environmental Engineering (DBCEE), 705 Engineering
Research Center, University of Cincinnati, Cincinnati, OH 45221-001, USA
c
Nanotechnology Research Group, Department of Environmental Science, Institute of Technology Sligo, Sligo, Ireland
d
Centre for Precision Engineering, Materials and Manufacturing Research (PEM), Institute of Technology Sligo, Sligo, Ireland
b
a r t i c l e
i n f o
Article history:
Received 30 December 2014
Received in revised form 24 March 2015
Accepted 31 March 2015
Available online 2 April 2015
Keywords:
Anti-microbial
Synthesis
Energy and environmental
Tunable wettability
Water contact angle (WCA)
Hydrophobic
Graphene heterojunctions
Reduced graphene oxide (rGO)
Fluoroalkylsilane
Doped titania
a b s t r a c t
Self-cleaning materials have gained considerable attention for both their unique properties and practical
applications in energy and environmental areas. Recent examples of many TiO2 -derived materials have
been illustrated to understand the fundamental principles of self-cleaning hydrophilic and hydrophobic
surfaces. Various models including those proposed by Wenzel, Cassie-Baxter and Miwa-Hashimoto are
discussed to explain the mechanism of self-cleaning. Examples of semiconductor surfaces exhibiting
the simultaneous occurrence of superhydrophilic and superhydrophobic domains on the same surface
are illustrated, which can have various advanced applications in microfluidics, printing, photovoltaic,
biomedical devices, anti-bacterial surfaces and water purification.
Several strategies to improve the efficiency of photocatalytic self-cleaning property have been discussed including doping with metals and non-metals, formation of hetero-junctions between TiO2 and
other low bandgap semiconductors, and fabrication of graphene based semiconductor nano-composites.
Different mechanisms such as band-gap narrowing, formation of localized energy levels within the
bandgap and formation of intrinsic defects such as oxygen vacancies have been suggested to account
for the improved activity of doped TiO2 photocatalysts. Various preparation routes for developing
efficient superhydrophilic–superhydrophobic patterns have been reviewed. In addition, reversible photocontrolled surfaces with tuneable hydrophilic/hydrophobic properties and its technological applications
are discussed. Examples of antireflective surfaces exhibiting self-cleaning properties for the applications
in solar cells and flat panel displays have also been provided. Discussion is provided on TiO2 based selfcleaning materials exhibiting hydrophilic and underwater superoleophobic properties and their utilities
in water management, antifouling applications and separation of oil in water emulsions are discussed.
In addition, ISO testing methods (ISO 27448: 2009, ISO 10678: 2010 and ISO 27447: 2009) for analysing
self-cleaning activity and antibacterial action have also been discussed. Rapid photocatalytic self-cleaning
testing methods using various photocatalytic activity indicator inks such as resazurin (Rz), basic blue 66
(BB66) and acid violet 7(AV7) for a broad range of materials such as commercial paints, tiles and glasses
are also described. Various commercial products such as glass, tiles, fabrics, cement and paint materials developed based on the principle of photo-induced hydrophilic conversion of TiO2 surfaces have
also been provided. The wide ranges of practical applications of self-cleaning photocatalytic materials
suggest further development to improve their efficiency and utilities. It was concluded that a rational
fabrication of multifunctional photocatalytic materials by integrating biological inspired structures with
tunable wettability would be favorable to address a number of existing environmental concerns.
© 2015 Published by Elsevier B.V.
Contents
1.
2.
Introduction . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Contact angle and wettability . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
397
397
∗ Corresponding author at: Center for Precision Engineering, Materials and Manufacturing Research (PEM), Institute of Technology Sligo, Sligo, Ireland. Tel.: +353 719305816.
E-mail address: Pillai.suresh@itsligo.ie (S.C. Pillai).
http://dx.doi.org/10.1016/j.apcatb.2015.03.058
0926-3373/© 2015 Published by Elsevier B.V.
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
3.
Photocatalytic hydrophilic surfaces . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Generation of light-induced surface vacancies . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
3.1.
3.2.
Photoinduced reconstruction of Ti OH bonds . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Photo-oxidation of adsorbed hydrocarbon . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
3.3.
A combination of various mechanisms . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
3.4.
Improving photocatalytic and self-cleaning activities of TiO2 . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.
4.1.
Impact of surface roughness and porosity on photocatalytic self-cleaning properties . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.2.
Non-metal doping . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Metal doping . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.3.
Metal-non-metal co-doping . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.4.
Dye sensitization . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.5.
4.6.
Heterojunction/heterostructure formation . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.6.1.
Graphene based heterostructures . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
TiO2 /SiO2 heterostructures for superhydrophilic and antireflective surfaces . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.6.2.
Summary of contact angles of various TiO2 composites . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
4.7.
5.
Photocatalytic antibacterial composites . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
6.
Photocatalytic hydrophobic surfaces . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
7.
Reversible photo-controlled wetting . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
8.
Underwater-superoleophobicity . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Other material displaying self-cleaning activity . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
9.
10.
Testing methods for photocatalytic self cleaning surfaces . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
10.1.
ISO 27448: 2009: Standard testing method for photocatalytic self-cleaning surfaces by measuring the contact angle . . . . . . . . . . . . . . . . .
10.2.
ISO 10678; 2010, ‘Determination of photocatalytic activity of surfaces in an aqueous medium by degradation of methylene blue’ . . .
ISO 27447: 2009, ‘Fine ceramics, advanced technical ceramics – test method for antibacterial activity of
10.3.
semiconducting photocatalytic materials’ . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
10.4.
Photocatalytic activity indicator inks . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
11.
Commercial applications of photocatalytic self cleaning surfaces . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
12.
Conclusions . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
Acknowledgements . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . .
1. Introduction
Development of self-cleaning materials, understanding their
structure-function relationship, and engineering artificial surfaces
with variable wettability suitable for various commercial applications constitute an active research domain in material science [1].
These materials have received substantial interest in recent years
due to their wide applications in various fields ranging from indoor
applications in fabrics [2–4], furnishing materials [5,6], window
glasses [7–9], to exterior construction materials, roof tiles [10,11],
car mirrors [5,6], and solar panels [12–14]. These materials can
easily be cleaned by a stream of natural water such as rainfall,
which in turn significantly reduces the routine maintenance cost.
Self-cleaning activity is predominant in nature, for example, in the
cases of leaves of lotus plant [15,16], rice plant [17], butterfly wings
[18], fish scales [19] etc. The waxy surface of lotus leaves combined
with the presence of microscopic structures result in an extremely
hydrophobic surface [20]. Consequently, when water droplets roll
off the leaves, the dust/dirt particles are also removed. This mechanism is widely known as “Lotus effect” [16]. Broadly, self-cleaning
surfaces can be divided into two categories: (i) hydrophilic surfaces
and (ii) hydrophobic surfaces [21,22]. In the case of hydrophilic
surfaces water drops spread over the surface and form a film of
water. During the process of spreading, the contaminants on the
surface are washed away (Fig. 1a). In the case of hydrophobic surfaces, the water drops roll off the surface quickly due to the water
repellent and low adhesive properties of hydrophobic surfaces,
and thereby remove the contaminants on the surface (Fig. 1b). A
great amount of work has been devoted in recent years to design
self-cleaning biomimetic surfaces displaying anti-fouling, antireflective properties [23–27]. Several reviews have been published
on self-cleaning action of TiO2 over the past years that mainly discuss photocatalytic activity of TiO2 [8,28–30]; however, there are
not many articles that deal with photocalytic self-cleaning activity
of TiO2 with particular emphasis on fundamental mechanism
397
400
400
402
402
402
403
404
404
406
406
407
408
409
409
411
411
412
414
415
416
417
417
418
419
419
421
424
425
425
of photoinduced hydrophilicity and its commercial applications
[21]. In the current review, a number of TiO2 based photocatalytic
materials are illustrated to understand the fundamental principles
of self-cleaning hydrophilic and hydrophobic surfaces. In addition,
composite materials containing self-cleaning materials exhibiting
hydrophilic and underwater superoleophobic properties and photocatalytic antibacterial activity are discussed in detail and recent
advances in the self-cleaning action by photocatalytic action are
comprehensively reviewed. In addition, detailed information on a
number of self-cleaning commercial products such as glass, tiles,
fabrics, cement and paint materials are discussed.
2. Contact angle and wettability
The wettability of a surface can be determined by measuring the
contact angle () of the liquid drop over the solid surface, which
is defined as the angle formed between the solid surface and the
tangent drawn at the liquid drop as shown in Fig. 2 and is a measure of the angle between solid–liquid and liquid–vapor interfaces.
At thermodynamic equilibrium condition between the solid, liquid
and vapor phases, the relation between the interfacial energies per
unit area is given by Young’s relation (Eq. (1)).
sv
=
SL
−
LV cos
(1)
where SV , SL and LV represent the interfacial energy per unit area
of the solid–vapor, solid–liquid and liquid–vapor interfaces and is
the contact angle. For partial or totally wettable surfaces the contact
angle is usually low (0◦ < < 90◦ ). For superhydrophilic surfaces
approaches to zero value ( < 5◦ ) and the liquid drop tends to evenly
spread on the surface (Table 1) [31,32].
Eq. (1) relate parameters such as , SV , SL and LV which
cannot usually be obtained experimentally [33,34]. In addition, it
was previously showed that the contact angle () measurement
is not always highly reproducible. The real contact angle , can
take any value within R ≤ ≤ A , (where A and R are defined
398
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 1. Schematic representation of self-cleaning processes on (a) a superhydrophilic and (b) a superhydrophobic surface.
(Reproduced from RSC Adv. 3 (2013) 671–690, with permissions from Royal Society of Chemistry).
Fig. 2. Schematic representation of a liquid drop in equilibrium on a hydrophilic and a hydrophobic surface.
Table 1
Relationship of contact angle values and wettability behavior.
Contact angle
Wettability
> 90◦
> 150◦
0◦ < < 90◦
< 10◦
Hydrophobic
Superhydophobic
Hydrophilic
Superhydrophilic
as the advancing and receding angles, respectively) and the difference between A and R is termed as hysteresis. Both R and A are
characteristic of the surface chemistry, texture and topography.
It should be noted here that Eq. (1) is valid only for ideal solid
surfaces, characterised by chemically homogeneous, inert, rigid and
smooth surfaces. The wettability properties of rough surfaces are
commonly described by the model proposed by Wenzel [35] and
the model by Cassie-Baxter (Fig. 3) [36].
According to the Wenzel model, for a rough surface, which has
higher surface area than a smooth surface, the liquid droplet forms
contact with the entire surface and completely penetrates into the
cavities on the surface. For such a rough surface the “apparent”
contact angle app for a liquid droplet is related to the “true” contact
angle s of the droplet on a smooth surface by the roughness factor
r of the surface as described in Eq. (2).
cos app = rcos s
(2)
where the surface roughness factor r is defined as the ratio of geometric surface area to the actual surface area (Eq. (3)).
r=
Geometric Surface Area
Actual Surface Area
Fig. 3. Effect of the surface structure on the wetting property of a solid surface.
(Reproduced from Adv. Colloid Interface Sci. 210 (2014) 47–57 with permissions from Elsevier).
(3)
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
399
Fig. 4. Effect of surface structure on the wetting behavior according to MiwaHashimoto surface model.
(Reproduced from Langmuir 26 (2010) 15875–15882 with permission from American Chemical Society).
The Wenzel equation predicts that hydrophilicity and
hydrophobicity of a surface depends on the nature of the corresponding surface. For a hydrophilic surface ( < 90◦ and r > 1), with
an increase in surface roughness, hydrophilicity also increases.
Conversely for a hydrophobic surface, ( > 90◦ and r > 1), surface
hydrophobicity increases with increasing surface roughness.
Although these trends are observed in most cases, Wenzel model
cannot satisfactorily deal with all heterogeneous surfaces.
The Cassie-Baxter model does not postulate complete penetration of a liquid droplet into the surface cavities. This model suggests
that the spreading of a liquid droplet on a rough surface destroys
the solid–vapor interface and forms solid–liquid and liquid–vapor
interfaces as shown in Fig. 3b. According to Cassie-Baxter model,
the “apparent” contact angle app for a liquid droplet on a rough
surface is related to the true contact angle by Eq. (4),
cosapp = fs coss +f v cosv
(4)
where fs and fv represent the area fraction of the liquid droplet in
contact with the solid surface and area fraction of the liquid droplet
in contact with the vapor trapped in the cavities on the rough surface, respectively, and v is the contact angle of the liquid in air. For
v = 180◦ , and fs + fv = 1, Eq. (4) can be written as,
cosapp = −1 + fs (coss +1)
(5)
Effects of the surface roughness on water contact angle of superhydrophobic surfaces were investigated by Miwa et al. [37]. Various
superhydrophobic surfaces with various roughness parameters
were compared. It has been observed that in superhydrophobic
region, the sliding angles decrease with increasing contact angle
depending on the surface roughness. This model combines the
Wenzel and the Cassie-Baxter models through the Eq. (6) and is
usually referred as Miwa-Hashimoto model [38].
′
cos = rMH fMH cos + fMH − 1
Fig. 5. Different types of hydrophilic, superhydrophilic and superhydrophobic surfaces found in nature and corresponding properties of bio-inspired surfaces.
(Reproduced from RSC Adv. 3 (2013) 671–690, with permissions from Royal Society
of Chemistry).
(6)
where ′ and represent the equilibrium contact angles on a rough
surface and on a flat surface, respectively; rMH is the ratio of the
side area to the bottom area of the needle (Fig. 4) and fMH is the
fraction of surface area of the material in contact with the liquid.
Various types of hydrophilic, superhydrophilic and superhydrophobic surfaces can be found in nature (Fig. 5). For example,
the contact angle of lotus leaf and butterfly wings are measured as
about 164◦ and 152◦ , respectively [22]. Functional materials and
surfaces created by understanding the mechanism of self-cleaning
surfaces found in the living nature are called bio-inspired process
[22].
The presence of superhydrophilic and superhydrophobic
domains on the same surface can have various applications in
microfluidics, printing, biomedical devices and water collection
[39–43]. Superhydrophobic–superhydrophilic micro patterned
films have been fabricated based on a three layered structure
consisting of a Al2 O3 gel film, a very thin TiO2 gel layer, and a
fluoroalkylsilane (FAS) layer [44]. The surface showed a WCA of
150◦ and the contact angle decreased sharply to 5◦ upon UV illumination. Irradiation with UV light initiates photocatalytic processes
in TiO2 , which in turn result in the cleavage of fluoroalkyl chain and
the FAS layer consequently convert to a silica layer. The hydrophilic
property of the surface is further enhanced due to the rough structure of Al2 O3 layer. Superhydrophobic TiO2 surfaces have been
developed by roughening the surface using radio-frequency plasma
with CF4 as an etchant [45]. The rough wedge-like TiO2 surface was
subsequently modified with a hydrophobic monolayer of octadecylphosphonic acid (ODP). TiO2 surfaces plasma etched for 10 s and
subsequent surface modification with ODP showed a WCA greater
than 150◦ . The surface was converted into a superhydrophilic
surface (WCA = 0◦ ) upon UV illumination, due to rapid decomposition of ODP coating resulting from TiO2 photocatalysis. The
superhydrophobicity was recovered by dipping the TiO2 surface
in a solution of ODP and the superhydrophilic/superhydrophobic
conversion was repeated for more than five cycles without any
significant loss in hydrophobicity, which suggests possibility
of designing superhydrophilic/superhydrophobic micro patterns
based on such structures, with sharp contrast in light induced wettability behavior. Superhydrophilic–superhydrophobic patterns
with tunable wettability have been developed using nanostructured TiO2 films modified with fluoroalkylsilanes (FAS) using
photocatalytic lithography technique [46,47]. The WCA on the
modified surface was found to be 156◦ attributed to the rough morphology of the surface and the wettability was found to change
drastically (WCA < 5◦ ) upon UV-exposure due to selective photocleavage of the fluoroalkyl chain assembled on TiO2 surface. The
generation of superhydrophilic–superhydrophobic micropatterns
can be used to fabricate various devices. For example, the fabrication of superhydrophilic–superhydrophobic patterns with a
resolution of 133 and 150 lines per inch on titanium substrates for
offset printing is reported [48]. The micropattern formation was
further used as a template to develop coating of nano octacalcium
400
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 6. Schematic illustration of various processes occurring after photoexcitation of pure TiO2 with UV light.
phosphate by electrochemical deposition [46]. Such micropatterns
with sharp contrast in wettability have been used to construct
three dimensional functional patterns for applications in biomedical devices for high throughput molecular sensing, drug delivery,
etc [49].
3. Photocatalytic hydrophilic surfaces
The photocatalytic hydrophilic surfaces utilize sunlight/indoor
light to decompose the dirt and other impurities [50–54]. TiO2
based photocatalysts have gained considerable attention as TiO2
exhibits significantly high physical and chemical stability, low
cost, easy availability, low toxicity and excellent photo-activity
[50,55–60]. In the presence of light of suitable energy (where, the
energy of the excitation source is higher than the band-gap energy
of the material), an electron (e− CB ) is excited from valence band
of TiO2 to the conduction band, generating a positive electron hole
(h+ VB ) in the valence band (Fig. 6). The photoexcited electron (e− CB )
can in turn recombine with the electron hole (h+ VB ) and reduce the
overall efficiency of the photoprocess. The charge carriers, which
can escape the charge-annihilation reaction, migrate to the surface,
where the photoexcited electrons can reduce atmospheric oxygen
to generate superoxide radicals (• O2 – ) or hydroperoxyl radicals
(HO2 • ). The valence band hole can also oxidize surface adsorbed
water or OH– and produce • OH. These reactive oxygen species
(ROS) can convert organic pollutants into CO2 and water resulting in the cleaning of the surface. A major limitation in developing
self-cleaning materials based on TiO2 is the wide band gap of the
semiconductor, limiting its absorption to the UV region of sunlight,
which comprises only 3–5% of the solar spectrum [57]. Due to this
wide band gap, utility of pure TiO2 is restricted in fabrication of selfcleaning materials (e.g., glass and tiles) for outdoor application. In
order to efficiently utilize the visible region of solar spectrum, several strategies have been developed [57], which will be discussed
in a later section.
Semiconductor + hv → h+ VB + e− CB
(7)
e− CB + h+ VB → Energy
(8)
h+ VB + H2 O → • OH + H+
e− CB + O2 → • O2 −
(9)
(10)
The superhydrophilic and oleophilic character of TiO2 was first
reported by Wang et al. [7]. A thin polycrystalline film of TiO2
(anatase) displayed a contact angle of 72 ± 1◦ for water in the
absence of light. Wang et al. reported that if the TiO2 film is irradiated with ultraviolet light, the contact angle reduced to 0◦ resulting
in a spreading of water droplets on the surface (Fig. 7). Similar
trend was also observed for oily liquids such as glycerol trioreate
and hexadecane [7]. The changes in wettability were observed for
both anatase and rutile TiO2 irrespective of their photocatalytic
properties. In recent years, thin films of anatase TiO2 nanowire
arrays with exposed highly reactive (0 0 1) facet have been synthesized through a fluorine free hydrothermal technique [61]. The
oriented anatase TiO2 thin films exhibited high transparency, photocatalytic activity and superhydrophilicity upon UV-irradiation,
which are advantageous for applications in self-cleaning coatings.
Self-cleaning materials have been developed from mono and selfassembled multilayer TiO2 nanosheets deposited on quartz glass
slides by layer by layer deposition technique [62]. The photocatalytic activities of the nanosheets were examined in terms of their
ability to degrade methylene blue dye. The photocatalytic efficiency
of TiO2 nanosheets was lower than the anatase TiO2 films and the
photobleaching rate decreased with increasing number of layers. A
cost-effective electrospinning technique has been recently developed to fabricate photocatalytic, superhydrophilic and optically
transparent TiO2 films suitable for applications in window coatings
and photovoltaic cells [63]. Several mechanisms have been proposed to account for the photoinduced hydrophilicity exhibited by
TiO2 including (i) generation of light-induced surface vacancies [7],
(ii) photoinduced reconstruction of surface hydroxyl groups [64,65]
and (iii) photoinduced removal of the carbonaceous layer present
on TiO2 surfaces exposed to air [66].
3.1. Generation of light-induced surface vacancies
The initial and widely accepted mechanism for photoinduced
hydrophilicity was proposed by Wang et al. which relies on the
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
401
Fig. 7. Photoinduced wettability switching, where a hydrophobic TiO2 surface (a) is converted into a superhydrophilic surface (b) upon UV-irradiation, (c) exposure of a
hydrophobic TiO2 -coated glass to water vapor results in the formation of fog (small water droplet), (d) antifogging effect induced by UV-illumination.
(Rreproduced from Nature 388 (1997) 431–432 with permission from Nature Publishing Group).
Fig. 8. Schematic representation of photo-induced hydrophilicity. Electrons reduce the Ti(IV)–Ti(III) state and thereby the oxygen atoms will be ejected (creation of oxygen
vacancies). Oxygen vacancies will increase the affinity for water molecules and thereby transforming the surface hydrophilic.
402
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
formation of surface defects upon UV light illumination [7]. Friction
force microscopic studies suggested that UV irradiation resulted
in a structural change at the TiO2 surface thereby influencing the
interfacial force along the solid–liquid boundary and consequently
changing the contact angle [67]. The surface of TiO2 consists of five
coordinated Ti atoms with the sixth position occupied by H2 O or
OH– . It is believed that UV irradiation creates oxygen vacancies
at the two coordinated oxygen bridging sites at the surface,
thereby converting Ti4+ ions to Ti3+ [67]. These defects can in turn
increase the affinity for hydroxyl ions formed by dissociation of
chemisorbed water molecules and thereby forming hydrophilic
domains (Fig. 8). Moreover, crystal planes (1 1 0) and (1 0 0) of
rutile TiO2 with bridging oxygen sites showed higher efficiency
for hydrophilic conversion compared to the planes such as (0 0 1)
without bridging oxygen sites [68,69]. Atomic force microscopic
study of UV-illuminated rutile TiO2 single crystal showed that
TiO2 surface consists of microscopic hydrophilic and oleopholic
domains, which are believed to generate capillary flow channels for
oil and water [67]. It was found that if the hydrophilic TiO2 material
is stored in dark for a couple of days, the hydrophilic character
gradually decrease due to slow replacement of the chemisorbed
hydroxyl and water molecules by oxygen molecules from air.
However, the hydrophilic nature of the surface can be retrieved by
further UV illumination. Nakajima et al. demonstrated the photoinduced amphiphilic surface formation for polycrystalline anatase
TiO2 thin films [70]. However, prolonged UV irradiation was shown
to convert the surface into a hydrophilic–oleophobic one, which
is considered to be due to variation in the rate of hydrophilic
conversion of TiO2 grains. Rutile TiO2 exhibited photoinduced
surface hardness correlated with the conversion of hydrophilic
surface [71]. This photo-induced change in surface hardness has
been attributed to surface volume expansion resulting from the
increase in distance between the adjacent Ti atoms arising from
the dissociative adsorption of water molecules upon UV exposure.
controlled atmospheric conditions [66]. According to their mechanism, the organic pollutant is photocatalytically degraded upon
UV-irradiation on a water droplet. With an increasing irradiation
time, photocatalytic degradation continues leading to a decrease
in the surface coverage by the contaminant. At the critical point,
where the surface coverage approaches zero (i.e., beyond the
perimeter of the water droplet), rapid spreading of water droplet
occurs.
Takeuchi et al. proposed that thermal energy of the irradiating
light can cause desorption of the weakly attached water molecules
from the surface of TiO2 [74]. As shown in Fig. 9, heating TiO2
thin film causes desorption of water molecules from the surface
and results in a decrease in H-bonded network on the surface and
decrease in surface tension of the water cluster, which is considered
to be crucial for the surface wetting. In the presence of UV irradiation, water desorption due to heating effect occurs simultaneously
with the photocatalytic degradation of organic contaminants leading to hydrophilic conversion. It should also be noted that the free
energy of cohesion of water does not significantly decrease with
temperature. The change in contact angle due to heating can also
be explained in such a way that, during water evaporation there will
be a reduction in size of the water droplet. Therefore, the receding
contact angle ( R ) will be smaller than the advancing contact angle
( A ) due to wide contact angle hysteresis.
Sakai et al. described the enhancement of hydrophilic conversion rate of TiO2 in the presence of UV illumination and high
electrode potential [65], which demonstrated the importance of
electronic photoexcitation rather than thermal action of the illuminating light. Yan et al. also demonstrated that photoinduced
hydrophilic conversion of TiO2 thin films occurs in two stages,
where in the first phase WCA decreases only when the surface is
illuminated with a monochromatic light of wavelength shorter than
the absorption edge, emphasizing the importance of photoinduced
electron–hole generation [75].
3.2. Photoinduced reconstruction of Ti OH bonds
3.4. A combination of various mechanisms
Sakai et al. demonstrated that the rate of hydrophilic conversion of TiO2 film electrode upon UV light irradiation was increased
at high positive electrode potentials and decreased in the presence
of hole scavenging agents [65]. Based on these observations, it was
suggested that the diffusion of photogenerated holes play an important role in the hydrophilic conversion. Subsequently to account
for photoinduced hydrophilic conversion of TiO2 surfaces, Sakai
et al. proposed that UV illumination results in the reconstruction of
hydroxyl groups at the surface [64]. The extent of hydrophilic conversion was linked to the density of surface hydroxyl group, which
in turn was correlated to the reciprocal of the contact angle. According to this model, the positive hole generated upon illumination of
TiO2 can diffuse to the surface and gets trapped at lattice oxygen.
Consequently, the binding energy between the Ti and lattice oxygen
becomes weak and water molecules can rupture this bond resulting in the formation of new hydroxyl bonds. In the absence of light,
the hydroxyl groups gradually desorb from the surface in the form
of H2 O2 or H2 O + O2 and the surface reverts back to the original less
hydrophilic state. Mechanical treatments such as ultrasonication
[72] and wet rubbing [73] can cause desorption of thermodynamically less stable hydroxyl groups induced by UV illumination and
make the surface less hydrophilic.
Guan explained the relationship of adsorption of water
molecules and hydrophilicity (Fig. 10). The water molecules will
initially be chemisorbed on the TiO2 surface and these water
molecules will further ‘adsorb’ water by physisorption (van der
Waals forces or hydrogen bounds) [76]. These physisorbed water
molecules will act as a barrier to prevent the close contact between
the surface and pollutants. Therefore, the pollutants which come
in contact with the surface will easily be removed by these loose
water molecules [76]. The synergistic effect of photocatalysis and
hydrophilicity will result in long-term self-cleaning activity. The
contact angle of the pure TiO2 coatings was about 10◦ and it reduces
below 5◦ when 40 mol% SiO2 was added. The high surface acidity
due to the presence of Si cations and its ability to adsorb more
hydroxyl group was the main reason for the reduced contact angle.
Several treatments such as alkaline wash and vacuum UV treatments, which remove organic contaminants from the surface, can
improve surface wettability; however, superhydrophilic surface
could not be obtained by these treatments. Moreover, the water
contact angle for several metal oxides such as tungsten oxide
and vanadium oxide, was found to decrease in response to UVirradiation. However, no significant photocatalytic activity was
detected, which suggests photocatalytic decomposition of surface
adsorbed pollutants cannot be solely responsible for the surface
wetting phenomenon [77]. The photoinduced hydrophilic surface of TiO2 gradually reverts back to the hydrophobic state in
the absence of UV-illumination and the rate of this conversion
was found to increase in pure oxygen atmosphere. If photocatalytic removal of hydrocarbon was the principal mechanism for
hydrophilicity, then hydrophilic–hydrophobic conversion should
3.3. Photo-oxidation of adsorbed hydrocarbon
In contrast to the widely accepted mechanism of surfacehydroxylation explaining the gradual hydrophilic conversion of
TiO2 induced by UV illumination, Zubkov et al. reported the
sudden onset of UV light induced surface wetting under highly
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
403
Fig. 9. (a) Schematic illustration of hydrophilicity arising from the photocatalyzed decomposition of hydrocarbons (reproduced from J. Phys. Chem. B 109 (2005) 15454–15462
with permission from American Chemical Society) and (b) suggested mechanism to improve surface wettability of TiO2 surface upon solar illumination (reproduced from J.
Phys. Chem. B 109 (2005) 15422–15428 with permission from American Chemical Society).
have been higher under ambient condition compared to oxygen
atmosphere due to higher concentration of hydrocarbon contaminants [77].
As evident from the above discussion, various hypotheses have
been proposed to account for the observed hydrophilic conversion of TiO2 surfaces; however, no consensus mechanism has been
elucidated so far to clarify the photoinduced superhydrophilicity.
Recently, Emeline et al. described that the efficiency of photoinduced superhydrophilic conversion depends strongly on the
intensity and wavelength of the actinic light, which suggests the
initial step involves photoexcitation of electrons and generation of
charge carriers [78]. Moreover, hydrophilic conversion was shown
to depend strongly on temperature and surface acidity indicating the involvement of external hydrate layers in the hydrophilic
conversion. Alteration of surface acidity was found to change the
efficiency of charge carrier trapping, which in turn changes the
interaction between the surface hydroxyl groups and outer hydrate
layers and vary the efficiency of the photoinduced hydrophilic conversion due to change in surface energy and entropy of the hydrate
layers [78].
4. Improving photocatalytic and self-cleaning activities of
TiO2
Due to the wide band gap of TiO2 (3.2 eV for anatase and
3.0 eV for rutile), light absorption by the semiconductor material
and consequently superhydrophilic conversion of undoped TiO2
are limited to only ultraviolet region (wavelength <390 nm) and
thereby restricting the practical uses of self-cleaning phenomenon
404
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
surfaces. Superhydrophilic TiO2 /SiO2 composite film containing
0.5 wt% polyethylene glycol (PEG), showed excellent antifogging
properties due to increased surface roughness, where the WCA
changed from 15◦ to 3◦ within 0.16 s [80]. The super-hydrophilic
titania films synthesized from alkoxide with PEG were studied to
understand the impact of porosity and contact angle [80]. As the
quantity and molecular weight of PEG increased, the porosity of
the resultant coating also increased after the heat treatment. The
OH groups adsorbed on the porous surface were found to increase
due to the larger surface area of these coatings. The water contact
angle measurement on the porous TiO2 coating showed correlation between superhydrophilic nature and number of surface
OH groups as well as surface roughness [81]. Porous titania coatings with super-hydrophilic properties were synthesized by the
carbonatation of amorphous Li–Ti–O. Porous TiO2 meso-channels
were created by a chemical etching process (Fig. 11) [82]. After
UV irradiation for 10 min, the contact angle on these highly porous
meso-channels was reduced below 5◦ [82].
4.2. Non-metal doping
Fig. 10. Self-cleaning mechanism by the adsorption of water.
(Reproduced from Surf. Coat. Technol. 191 (2005) 155–160 with permissions from
Elsevier).
to outdoor applications only. Additionally, rapid electron–hole
recombination also limits utility of pure TiO2 based materials.
4.1. Impact of surface roughness and porosity on photocatalytic
self-cleaning properties
It has been noted by a number of authors that the contact angle
of a surface is highly depended on the texture of the surface [79].
Lee et al. investigated the relationship of surface roughness and
hydrophilicity and showed that the contact angle of rough titania
surface was 15◦ , while the smooth titania surfaces showed a contact angle of 70◦ . It has also been shown that the recovery rate
to hydrophilicity under UV irradiation had a reverse dependence
on the surface roughness. The rough titania surface can have a
high concentration of Ti3+ produced by UV irradiation and these
non-stoichiometric species on the surface play the pivotal role
as adsorption sites of − OH from water molecules [72,79]. Formation of highly porous structure to increase the surface roughness
appeared as an alternative approach to achieve superhydrophilic
Fig. 11. Formation of porous TiO2 channels.
In order to utilize the sunlight/interior light effectively and to
overcome the rapid charge carrier recombination, various research
groups have developed metal and non-metal doped TiO2 . Doping
with non-metallic elements such as N [83–86], C [87–93], and S
[94,95] has shown to enhance the visible light absorption of TiO2 .
Several mechanisms have been proposed to account for the shift in
absorption band, including band gap narrowing resulting from the
mixing of orbitals of TiO2 and impurity [96], generation of oxygen
vacancies [97], and formation of localized energy levels in the band
gap (Fig. 12) [98–101].
Asahi et al. demonstrated that N-doped TiO2 exhibited efficient
degradation of organic pollutants upon visible light irradiation
[96]. The TiO2−x Nx film with a 5 nm thick SiO2 coating to hold
the adsorbed water showed conversion to hydrophilic surface
with a contact angle of 6◦ upon interior light exposure [96]. The
hydrophilic nature of the surface was maintained even after 30
days. Irie et al. subsequently reported the correlation between
the hydrophilic conversions to the extent of dopant nitrogen concentrations under irradiation with visible light [102]. The visible
light activity of the N doped TiO2 thin film was thought to be
arising from localized N centred 2p orbitals. The rate for the
hydrophilic conversion increased and the critical contact angle
decreased with increasing the concentrations of doped nitrogen
for various TiO2−x Nx films. The enhanced hydrophilicity obtained
with increasing the extent of N substitution was ascribed to an
increase in absorbed photons. Visible light active N-doped TiO2
thin films were also prepared using magnetron sputtering [103].
(Reproduced from Thin Solid Films 516 (2008) 3888–3892 with permission from Elsevier).
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
405
Fig. 13. Changes in contact angle of C-doped TiO2 under UV and vis irradiation conditions.
(Reproduced from Thin Solid Films 510 (2006) 21–25 with permission from Elsevier).
Fig. 12. Formation of localized energy levels in the band gap due to nitrogen doping
into titanium dioxide photocatalyst [85].
(Reproduced from J. Hazard. Mater. 211–212 (2012) 88–94 with permission from
Elsevier).
The visible light activity of TiO2−x Nx films has been assigned to
the band gap narrowing resulting from the shift of the top edge
of the valence band toward negative direction due to mixing of 2p
orbitals of N and O as well as anodic shifting of the bottom edge
of the conduction band due to the formation of oxygen vacancies.
TiO2−x Nx thin film electrode was converted to a hydrophilic one
under visible light illumination and application of anodic oxidation potential. The extent of hydrophilic conversion was found to
increase with increasing anodic potential possibly due to efficient
separation of the charge carriers. N-doped visible light active TiO2
thin films demonstrated photocatalytic degradation of organic pollutants and antimicrobial activity [104]. The N-doped films also
exhibited superhydrophilicity (water contact angle or WCA <5◦ )
under white light illumination. Surface wetting was also observed
in the absence of light. The superhydrophilicity presumably results
from the combined effect of improved photocatalytic activity and
the porous structure of the material. The activity of the N-doped
TiO2 films were further enhanced in the presence of Ag nanoparticles formed in situ on the surface of TiO2 films [104].
TiO2 thin films doped with various concentrations of carbon (1.1,
0.9, 0.7 mol%) have been prepared that undergo hydrophilic conversion (WCA <5◦ ) under UV and visible light irradiation (Fig. 13) [105].
It has been suggested that at lower concentration of the dopant
(0.7 mol%), isolated energy states corresponding to C 2p orbital in
the band gap account for the visible light activity. However, at the
higher concentration of the dopant (1.1 mol%), band gap narrowing
occurs due to mixing of 2p orbitals of carbon and oxygen in addition
to the presence of localized dopant based energy levels.
Surface fluorination of TiO2 has resulted in improved
hydrophilicity upon UV irradiation, due to increased adsorption
of water and other polar molecules, which is attributable to the
enhanced acidity [106]. Additionally, fluorination is also thought
to favor formation of Ti3+ through charge compensation between
Ti4+ and F− , which promotes charge carrier separation resulting in
an efficient photocatalytic conversion [107].
Co-doping TiO2 with two or more elements such as S–N [108],
C–N [109,110], N–F [111–113] has been found to be an effective
strategy to enhance the visible light induced photocatalytic activity
and inhibit charge carrier recombination. N, S-co-doped TiO2 thin
film synthesized through radio-frequency (RF) sputtering method
demonstrated higher visible light induced photocatalytic activity
than the N and S-doped TiO2 [114]. The N, S-co-doped TiO2 film also
exhibited better photoinduced hydrophilic conversion compared
to undoped TiO2 under fluorescent light bulb irradiation. Ab initio
calculations suggested that the improved activity of N,S-co-doped
TiO2 presumably results from bandgap narrowing due to mixing of
N 2p, S 3p and O 2p orbitals [114].
N–F co-doped TiO2 synthesized by a fluorosurfactant based
modified sol–gel technique, showed improved visible light
response and slow hydrophilic conversion with a WCA 8◦ upon
illumination with visible light for 14 days [115]. Two separate
wetting stages were observed for the N,F–TiO2 films, where in
the first phase the contact angle decreased up to 40◦ , while the
second phase representing the transition to hydrophilic state (contact angle below 20◦ ). The photocatalytic activity of the N,F–TiO2
films were found to be correlated with their hydrophilic conversion
properties. The improved wettability and photocatalytic activity of
the N,F-co-doped TiO2 films compared to undoped TiO2 have been
assigned to the rough and porous structure of the co-doped TiO2 ,
which suggests promising use of these materials in self-cleaning
applications.
C–N–F-co-doped TiO2 films possessing self-cleaning property
have been fabricated by a layer-by-layer dip-coating method using
TiO2 sol and NH4 F as precursors [116]. The C–N–F-co-doped TiO2
film exhibited enhanced photocatalytic degradation of stearic acid
under visible light irradiation, which has been assigned to the synergistic effect of the doped C, N and F atoms and the high surface
area of the photocatalyst.
N,F-co-doped TiO2 nanotube arrays with dispersed PdO
nanoparticles have been developed that showed higher visible light
absorption compared to N,F-co-doped TiO2 [117]. The enhanced
visible light absorption possibly results from the synergistic effect
of N,F co-doping combined with higher crystal lattice distortion of the nanotube structure. It has also been suggested that
metallic Pd◦ nanoparticles are generated by visible light induced
reduction of PdO nanoparticles and the surface plasmon resonance of Pd◦ nanoparticles also accounts for the visible light
activity of these nanocomposites. The N,F-co-doped TiO2 /PdO nanotube arrays exhibited enhanced photocatalytic activity and rapid
conversion to superhydrophilic surface upon visible light illumination [117]. The improved visible light induced response has
been explained in terms of optoelectronic coupling between N,F-
406
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 14. (a) Schematic illustration of the visible light induced electronic transitions for a C–Nd co-doped TiO2 sample, showing transitions from unoccupied Nd–4f energy
levels to the TiO2 conduction band, C-centred energy levels to the Nd-energy states as well as to the conduction band of TiO2 (reprinted from J. Phys. Chem. C 117 (2013)
8345–8352 with permission from American Chemical Society, (b) schematic representation of photoprocesses in a C–V co-doped TiO2 , where C on the surface of TiO2 acts
as a sensitiser, absorbs visible light and transfers electron to the conduction band or impurity energy levels, while V-doping into TiO2 lattice results in a band gap narrowing
(reprinted from ACS Appl. Mater. Interfaces 3 (2011) 1757–1764 with permission from American Chemical Society).
co-doped TiO2 and PdO nanoparticles, which favors trapping of
photogenerated electrons by PdO nanoparticles thereby inhibiting
electron–hole recombination.
4.3. Metal doping
Photocatalytic activity and visible light response of TiO2 can be
enhanced by doping with various metal ions, including 3d transition metal ions [118–122], lanthanides [123–125], and noble
metals [126–130]. Various mechanisms such as bandgap narrowing, formation of impurity based energy levels within the bandgap
and formation of intrinsic defects such as oxygen vacancies and
interstitial Ti have been suggested to account for the improved
activity of metal ion doped TiO2 . Y2 O3 doped TiO2 nanocomposite
film deposited on indium tin oxide (ITO) glass substrate has been
fabricated using sol–gel–dip coating technique [131]. The Y2 O3
doped TiO2 film was converted into a hydrophilic surface (WCA 8◦ )
upon illumination with a daylight lamp for 1 h [131]. A significantly
high number of oxygen vacancies can be created by the addition of
Y2 O3 into TiO2 during the UV irradiation [131,132]. These oxygen
vacancies are responsible for the hydrophilicity of the Y2 O3 –TiO2
nanocomposite film.V2 O5 –TiO2 nanoporous layers (pore size of
50–400 nm) were synthesized using micro-arc oxidation method
that exhibited higher hydrophilicity upon visible light illumination due to their rough surface [133]. Visible light absorption arises
from the doping of V2 O5 in the TiO2 lattice resulting in a narrow
band gap. Zang et al. reported the visible-light photo-degradation
of 4-chlorophenol in aqueous solution using amorphous microporous metal oxides of titanium (AMM-Ti) loaded with chlorides
of PtIV , IrIV , RhIII , AuIII , PdII , CoII , and NiII [134]. It was proposed that
the metal salts perform as chromophores, transferring the charges
generated during the photo-reactions to the amorphous region.
Modification of TiO2 lattice with varying amount of Zn2+ ion
was found to enhance the photocatalytic activity and visible light
absorption of TiO2 , which has been assigned to the formation of
surface oxygen vacancies, resulting in various sub energy levels situated near the bottom edge of the conduction band of TiO2 , which
are responsible for the visible light absorption of Zn-doped TiO2
[135]. Moreover, Zn2+ doped anatase TiO2 films deposited on ITO
glasses showed improved hydrophilicity compared to the undoped
TiO2 films due to formation of surface oxygen vacancies [136].
Co-addition of Zn2+ and an anionic surfactant sodium dodecylbenzenesulfonate (DBS) in the precursor sol increased the surface
roughness of TiO2 films and resulted in a superhydrophilic surface
(WCA 3◦ ), which was found to be maintained for two weeks in dark
[136].
4.4. Metal-non-metal co-doping
Co-doping TiO2 using both metal and non-metal elements have
gained considerable attention. The co-doped systems such as N–Cu
[39], N–Fe [137], N–W [138], V–N [139], C–Mo [140], C–Nd [141],
S–Fe [142], etc showed higher photocatalytic activity due to the
synergistic effects of metal and non-metal dopants. The doped
metal and non-metal elements can create additional energy levels
in the band gap (Fig. 14a). Upon visible light the electronic transition can occur from the valence band of TiO2 to the metal centred
energy levels as well as from doped non-metal based energy levels to the metal energy levels and TiO2 conduction band (Fig. 14a)
thereby increasing the overall visible light absorption [137–139].
Alternatively, the metal element can substitute at the Ti site in the
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
407
Fig. 15. Schematic representation of the electron/hole transfer mechanism for the B–Ag codoped TiO2 under solar irradiation.
(Reprinted from J. Am. Chem. Soc. 135 (2013) 1607–1616, with permission from American Chemical Society).
lattice while the non-metal can exist as a surface species (Fig. 14b).
The visible light activity of the co-doped TiO2 increases due to
the synergistic effects of metal and non-metal dopants, resulting
from the narrow band gap and separation of electron–hole pair
[143,144]. Recently, Feng et al. demonstrated the extraordinarily
high photocatalytic activity of B-Ag-co-doped TiO2 under solar irradiation [145]. It has been suggested that doped B species can weave
into the interstitial sites of the TiO2 lattice. Incorporation of Ag in
the close proximity of the tri-coordinated interstitial B (Bint ) sites
favors the formation of Bint –O–Ag structural units, which can trap
the photoinduced electron and facilitate electron–hole separation
(Fig. 15).
4.5. Dye sensitization
Sensitization of TiO2 by a visible light absorbing dye has been
widely used in semiconductor photocatalysis, for the degradation of organic pollutants as well as in dye sensitized solar cells
[146–149]. The sensitization process involves photoexcitation of
a sensitizer molecule (usually a transition metal complex or an
organic dye) to the appropriate singlet or triplet electronic excited
state, followed by an electron injection from the excited sensitizer molecule into the conduction band of semiconductor material.
The resulting electron–hole pair can in turn generate various reactive oxygen species that lead to degradation of organic pollutants.
Metalloporphyrins, and ruthenium complexes are considered as
efficient sensitizers due to the presence of delocalized electron systems and strong absorption in the visible region and high
thermal and chemical stability [150–154]. In addition to Ru(II) complexes and metalloporphyrins, other metal complexes based on
Os(II) [155], Pt(II)[156] and Re(I) [157] have also been extensively
used as sensitizers.
Visible light active self-cleaning cotton fibers functionalized
with
TiO2
have
been
developed
using
meso-tetra(4-carboxyphenyl) porphyrin (TCPP) and meso-tetra(4carboxyphenyl)-porphyrinato M(II) (MTCPP: M = Fe, Co, Cu, Zn)
sensitizers (Fig. 16) [151,158]. The photocatalytic self-cleaning
properties of the functionalized cotton fibers have been assessed
by their ability to remove coffee/wine stain under visible light
irradiation. Free base TCPP/cotton fibers exhibited lower photostability compared to the M-TCPP/cotton, thereby limiting the use of
TCPP as a sensitizer in practical self-cleaning applications. Among
Fig. 16. Schematic illustration showing the mechanism of dye sensitization in cotton functionalized with TiO2 and Cu–TCPP.
(Reprinted from ACS. Appl. Mater. Interfaces 5 (2013) 4753–4759 with permission from American Chemical Society).
408
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 17. Catechol–thiophene light harvesting molecules for dye-sensitization.
(Reproduced from J. Phys. Chem. C (114) 2010 17964–17974 with permission from
the American Chemical Society).
the metalloporphyrins, CuTCPP showed higher photocatalytic
activity.
A new type of dye-sensitized TiO2 system is reported using a
simple thiophene-catechol system (Fig. 17) [159]. In this case, the
charge transfer follows through a type II injection system, where
the charge injection occurs directly from the HOMO (highest occupied molecular orbital) of the organic system to the conduction
band of titania. (Fig. 17) [159]. The device performances were
optimized in relation to the dye loading, open circuit voltage and
current density. The light harvesting efficiency was consistent with
the level of conjugation (e.g., with 1, 2 or 3 thiophene units).
4.6. Heterojunction/heterostructure formation
Formation of heterojunction structures incorporating TiO2 and
other narrow bandgap semiconductor material is an attractive
strategy to improve the photostability and efficiency of photocatalytic processes by increasing the separation between charge
carriers. Various heterojunction structures such as ZnO/TiO2
nanocomposites [160], anatase–rutile or anatase-brookite TiO2
heterojunctions [161–164], have been developed for improving
photocatalytic reactions.
The hybrid film of TiO2 /WO3 (Fig. 18) was developed by depositing WO3 particles on a TiO2 film that exhibited an enhanced rate
for photocatalytic oxidation of methylene blue and transformed
to a highly hydrophilic surface upon illumination with a 10 W
Fig. 19. Schematic diagram demonstrating the charge transfer between ZnO and
TiO2 nanotube arrays.
(Reproduced from J. Mater. Chem. A 2 (2014) 7313–7318 with permission from Royal
Society of Chemistry).
fluorescent lamp [165,166]. The smaller band gap of WO3 (2.8 eV),
allows excitation by visible light, where photogenerated holes can
be transferred to TiO2 , which take part in subsequent photocatalytic oxidation reactions and hydrophilic conversion. Presence of
an intermediate SiO2 later between TiO2 and WO3 was found to
inhibit the charge migration and photoinduced processes. Pt or
other multielectron cocatalysts can accept electron from the conduction band of WO3 and thus facilitates the charge separation and
photocatalytic process [167]. TiO2 /WO3 bilayer films having low
W(VI)/Ti(IV) molar ratio were generated by layer-by-layer technique [168]. A high photonic efficiency (1.5%) was reported for
30 TiO2 /WO3 bilayers for the degradation of acetaldehyde (1 ppm)
upon UV-illumination.
Hierarchical flake like Bi2 MoO6 /TiO2 bilayer films have been
developed, which showed significantly enhanced photocatalytic
activity and self-cleaning properties under visible light irradiation
[169]. The porous and flake like structure of the hybrid material
provide higher surface area for efficient visible light harvesting coupled with efficient separation of electron and holes at the interface
of two semiconductors. In order to obtain low band gap material,
anatase TiO2 /Cr-doped TiO2 composite thin film deposited on glass
slide was developed using DC magnetron sputtering [170]. The
composite film showed significantly improved hydrophilicity than
the TiO2 thin film with the WCA reaching a value of 10◦ upon 5 h of
UV illumination. The enhanced hydrophilicity of the composite film
has been assigned to the effective charge separation at the interface. The anatase TiO2 /4.8% Cr-doped TiO2 exhibited the slowest
Fig. 18. Schematic illustration of photoinduced electron transfer in TiO2 /WO3 heterojunction in bilayer films.
(Reproduced from ACS Appl. Mater. Interfaces 6 (2014) 16859–16866, with permission from American Chemical Society).
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
409
TiO2 /reduced graphene oxide (RGO) hybrid films have been
developed by a combination of surface sol–gel process and layerby-layer assembly method [179]. The hybrid film showed improved
photocurrent generation under broadband light illumination,
where RGO can be photoexcited under both UV and visible-NIR
irradiation, while TiO2 is photoactive under UV radiation, resulting
in the overall broadband response of the hybrid film. Additionally,
photoexcited electrons from the conduction band of TiO2 can be
injected into RGO, which supresses charge carrier recombination
through rapid charge transport and charge separation. The hybrid
TiO2 /RGO film was converted into a superhydrophilic one with a
WCA 4.2◦ after broadband light illumination and exhibited excellent antifogging properties, which suggest potential utility of these
films in designing self-cleaning optoelectronic devices.
Fig. 20. Schematic illustration showing charge transfer in graphene/TiO2 composite.
(Reprinted from ACS Appl. Mater. Interfaces 5 (2012) 207–212 with permission from
American Chemical Society).
conversion into a hydrophobic surface and retained hydrophilicity
for 48 h after the UV-illumination was discontinued.
ZnO/TiO2 core–shell nanorod arrays (Fig. 19) have been further
developed by coating ZnO nanorods with a thin TiO2 nanosheet
with exposed (0 0 1) facets through a hydrothermal method [171].
Presence of the TiO2 coating provided chemical stability and
imparted enhanced photocatalytic activity and hydrophilicity. The
improved photocatalytic activity results from the combination
of enhanced surface area of the heterojunction photocatalyst
and increased charge separation resulting from the injection of
photoexcited electron from the conduction band of TiO2 to the conduction band of ZnO and the transfer of photogenerated holes of
ZnO to the valence band of TiO2 . The heterojunction coating displayed high transmittance and hydrophilicity (WCA 10◦ ) upon UV
irradiation owing to the highly porous structure of the nanorod
arrays. Transparent thin films of TiO2 –ZnO were deposited on polycarbonate sheets using interlayers of SiO2 [172]. The self-cleaning
coating with a TiO2 :ZnO molar ratio of 1:0.05 showed the most
efficient photocatalytic activity and superhydrophilicity under prolonged UV irradiation. Visible light active TiO2 /multiwalled carbon
nanotube (CNT) heterostructures have been fabricated by atmospheric pressure chemical vapor deposition technique [173]. The
TiO2 /CNT showed superhydrophilicity upon exposure to UV/vis
light due to slow recombination of electron and hole at the interface. Application of electric bias, also converted the TiO2 /CNT
surface into a superhydrophilic one due to formation of p–n junction at the interface.
4.6.1. Graphene based heterostructures
In recent years, nanocomposites of graphene with semiconductor materials have been found to exhibit improved optoelectronic
and photocatalytic properties [174–176]. Highly conductive and
optically transparent thin films comprising of graphene loaded
TiO2 showed significantly enhanced photocatalytic properties and
superhydrophilicity compared to pure TiO2 under illumination
from a white fluorescent lamp [177]. The enhanced photocatalytic activity of graphene/TiO2 can be attributed to the efficient
electron injection from the conduction band of TiO2 to graphene
(Fig. 20). The water contact angle for the graphene loaded TiO2
film decreased with increasing irradiation time. However, the film
did not show hydrophilic conversion under visible light, indicating
that only the UV portion of the white fluorescent light was effective for photoinduced hydrophilic conversion. Electroconductive
cotton fibers coated with TiO2 /graphene nanocomposite exhibited
improved self-cleaning and antimicrobial properties under UV and
solar irradiation [178].
4.6.2. TiO2 /SiO2 heterostructures for superhydrophilic and
antireflective surfaces
Self-cleaning TiO2 coatings with low surface reflection/antireflection property and high light transmission ability is
beneficial for their applications such as in flat panel displays, solar
energy collectors, and greenhouses [180–187]. Additionally, for
practical applications, it is desirable that the hydrophilic character
of self-cleaning coatings is maintained for a long period even in
the absence of light. However, photoinduced superhydrophilic
character of pure TiO2 film generally reverts back gradually in
the absence of light illumination. TiO2 /SiO2 composite films were
found to exhibit enhanced superhydrophilicity and improved
maintenance of hydrophilicity in dark [188–192]. The TiO2 /SiO2
composite films showed increased Lewis acidity resulting from the
excess positive charge generated due to the doping of silicon atoms
into the TiO2 lattice [193]. Increased acidity of the composite films
also accounts for the increase in the hydroxyl groups at the surface,
resulting in an enhanced hydrophilicity. Additionally, presence
of SiO2 can also decrease the refractive index of the TiO2 /SiO2
composite film and increase the extent of light absorption by the
composite film and hence increase the photocatalytic activity
[194,195]. Photocatalytic activity of TiO2 /SiO2 composite films was
found to be closely related to their hydrophilic property (Fig. 21)
[76,196].
Macroporous superhydrophilic TiO2 /SiO2 composite was also
developed using a template free sol–gel method that involved mixing the precursors of TiO2 sol and SiO2 sol in the presence of two
complexing agents, acetyl acetone and diethanolamine, to control
the rate of hydrolysis and precipitation of metal alkoxide [197].
Presence of SiO2 layer has also been reported to enhance the photocatalytic antibacterial property of TiO2 films [198]. TiO2 /SiO2
composite films doped with 3d metals have been prepared by
sol–gel dip coating technique, which showed red shifted absorption
compared to TiO2 /SiO2 composite and photoinduced superhydrophilicity [199,200]. Doped metal ions act as hole trapping
sites, which enhance the charge carrier separation and account
for the enhanced photocatalytic and self-cleaning properties. In
recent years, several groups have reported fabrication of superhydrophilic wool and cotton fibers using TiO2 /SiO2 composites,
which displayed photocatalytic self-cleaning activity against bacterial adhesion [198] and for removal of food, coffee and wine strains
[201–204].
Antireflective, self-cleaning coatings have been developed
using layer-by-layer assembly of SiO2 –TiO2 core–shell nanoparticles on glass support, that exhibit superhydrophilicity both in the
presence and absence of UV illumination [185,205]. The antireflection property arises from the presence of submicrometer sized
SiO2 particle layer, which also provided a porous structure. The
superhydrophilic property of the coatings results from enhanced
surface area of the nanoparticles and higher surface roughness of the particle coating. In order to produce antireflective
410
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 21. (a) High resolution electron micrograph of TiO2 /SiO2 nanocomposite containing anatase TiO2 synthesized in the presence of oxalic acid and polydimethyl siloxane,
(b) 3D AFM image of the nanocomposite, (c) optical microscopic image of an uncoated marble surface treated with methylene blue after UV irradiation, (d) microscopic image
of the methylene blue treated marble surface coated with TiO2 /SiO2 nanocomposite following UV illumination.
(Reproduced from Appl. Catal. B 156–157 (2014) 416–427, with permission from Elsevier).
self-cleaning coatings, TiO2 particles were used to coat
poly(ethylene terephthalate) [206] and poly(methyl methacrylate)
[207] films having moth-eye-like surfaces. The antireflection and
self-cleaning properties of the coatings can be applied in solar
cells and flat panel displays. Dust and other organic pollutants can
typically reduce the conversion efficiency up to 30% and therefore
the application of a self-cleaning coating can significantly improve
the efficiency of solar cells [208]. On the other hand, the lightabsorbing materials coated solar cells could decrease the overall
light to electricity conversion efficiency. No significant studies
have been found so far on the impact of hydrophilic self-cleaning
coatings on the light conversion efficiency [209]. Low cost antireflection coatings possessing self-cleaning properties have been
designed employing a self-assembled block copolymer in combination with silica sol–gel chemistry and anatase TiO2 nanocrystals
[210]. In order to overcome the problem associated with polymer
instability during outdoor applications of antireflective coatings,
hydrophobic surfaces were fabricated from vertically oriented
rutile nanorods grown on glass surface [211]. The resulting glass
substrates demonstrated high transmittance in the visible light
region (520–800 nm) and enhanced photocatalytic self-cleaning
activity toward hydrophilic and oily contaminants. The nature of
the solvent present in the precursor solution showed significant
effects on the nucleation and growth of the nanorods and played
crucial roles in determining the microstructure and morphology
of the surface (Fig. 22).
Fig. 22. Field emission scanning electronic microscopic images showing the effect
of solvent composition present in the precursor solution on the morphology and
water contact angle of TiO2 nanorods deposited on glass substrate.
(Reproduced from J. Colloid Interface Sci. 365 (2012) 308–313, with permission from
Elsevier).
411
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Table 2
Summary of contact angles of various TiO2 composites discussed.
System
Contact angle
Illuminating source
Intensity of illumination
Reference
PdO–N,F–TiO2
WO3 /TiO2
Bi2 MoO6 /TiO2
CNT/TiO2
SiO2 /TiO2
DBS–Zn–TiO2
C,N,F–TiO2
RGO/TiO2
V2 O5 –TiO2
Graphene/TiO2
Ag–N–TiO2
N–TiO2
C–TiO2
SiO2 /N–TiO2
Y2 O3 –TiO2
N,F–TiO2
TiO2 /Cr–TiO2
ZnO/TiO2
C–TiO2
N,S–TiO2
Zn–TiO2
0◦
0◦
0–12◦ (depending on reactime time)
0◦
3◦
3◦
3–4◦
4.2◦
<5◦
<5◦
<5◦
<5◦
<5◦
6◦
8◦
8◦
<10◦
10◦
>10◦
>10◦
27◦
Visible light <4 min
UV > 10 h
UV
Visible light 10 min
UV
Visible light
Measured in dark
Broadband illumination
UV (25 W lamp) for 45 min
While fluorescence light
White light for 2 h
White light for 2 h
UV > 1.5 h
Visible light for 30 days
Daylight lamp (60 W) irradiation for 60 min
Visible > 5 h
UV for 5 h
UV illumination
Visible > 1.5 h
Visible > 1 h
Visible light
1.0 mW/cm2
5–10 W/cm2
Not specified
Not specified
Not specified
Not specified
–
Not specified
Not specified
20 W/cm2
Not specified
Not specified
0.2 mW/cm2
159.4 W/cm2
Not specified
3 mW/cm2
0.5 mW/cm2
Not specified
0.2 mW/cm2
0.5 mW/cm2
Not specified
[117]
[166]
[169]
[173]
[80]
[136]
[212]
[179]
[133]
[177]
[104]
[104]
[105]
[96]
[131]
[115]
[170]
[171]
[105]
[114]
[136]
4.7. Summary of contact angles of various TiO2 composites
As discussed in previous sections, several strategies have been
developed by various groups to improve the photocatalytic activity and hydrophilicity of TiO2 based materials. Although there is
no straight forward way to compare the activity of various materials due to variation in the nature of illuminating light, intensity of
light, irradiation time, contact angle values, the systems were compared to obtain a general idea about the efficiency of self-cleaning
of different types TiO2 reported and are summarized in Table 2.
In general, modifications that increased surface roughness, for
example C,N,F co-doping [212], co-addition of Zn and DBS [136]
etc., appeared a promising way to increase the self-cleaning activity of the materials and also useful for maintaining hydrophilicity
upon storage in dark. Formation of heterostructure of TiO2 with
other materials to increase the charge separation appeared another
effective approach to increase the photocatalytic activity and selfcleaning efficiency. Introduction of rough surface morphology in
combination to heterostructure formation was found to be more
effective for fabrication of photocatalytic self-cleaning materials.
This was illustrated by the examples of Bi2 MoO6 /TiO2 [169] and
ZnO/TiO2 [171] systems. Doping with non-metals, especially nitrogen, was found to increase the hydrophilicity and visible light
induced photocatalytic activity [96].
5. Photocatalytic antibacterial composites
In recent years TiO2 based photocatalysts have gained significant attention for developing self-cleaning antibacterial materials
[213,214]. Kikuchi et al. initially demonstrated the UV-light
induced photocatalytic antibacterial activity of TiO2 thin films
[215]. TiO2 microspheres with reactive (1 1 1) facets exposed on
the external surface produced higher amount of • OH compared
to Evonik Degussa P25 upon UV illumination and demonstrated
higher rate of bacterial inactivation, which results from the suppressed electron–hole recombination in crystallized faceted TiO2
microsphere structures [216]. Visible light absorbing Cux O/TiO2
nanocomposites have been developed for indoor applications,
where the Cux O clusters composed of a mixture of Cu(II) and
Cu(I) species [217]. Presence of Cu(II) favored induced visible light
absorption of TiO2 and photocatalytic oxidation of volatile organic
compounds, while Cu(I) imparted antimicrobial activity in the
absence of light [217].
Visible light active C-doped anatase-brookite nanoheterojunction displayed significantly higher photocatalytic activity and
higher rate of inactivation against Staphylococcus aureus compared to commercially available photocatalyst Evonik-Degussa
P-25 [162]. S. aureus inactivation rate constants of 0.0023 and
−0.0081 min−1 were found for TiO2 hetero-junctions and Evonik
Degussa P-25, respectively. The efficient electron–hole separation at the TiO2 hetero-junctions interface is accountable for
greater antibacterial activity of the carbon doped TiO2 nanoheterojunctions. Photocatalytic disinfection of Escherichia coli, S.
aureus, Enterococcus faecalis, Candida albicans and Aspergillus niger
using C-doped visible light photocatalysts was also reported and
the inactivation was found in the following order E. coli > S.
aureus ≈ E. faecalis » C. albicans ≈ A. niger [218]. Anatase TiO2 nanotubes fabricated on Ti surface and loaded with Ag nanoparticles
demonstrated high antibacterial activity against E. coli [219]. To
achieve long-term antibacterial activity, Ag nanoparticles were
generated in situ within TiO2 nanotubes, coated with a quaternary
ammonium salt. The resulting nanocomposites exhibited high biocompatibility and long-term antibacterial activity. Presence of the
quaternary ammonium salt coating resulted in a reduced release of
Ag from the nanocomposites [220]. Anti-bacterial properties of undoped titania nano-tubes prepared by electrochemical anodization
method have also been analysed using E. coli and S. aureus. These
nanotube materials were found to be very effective in disinfecting both E. coli (97.5%) and S. aureus (99.9%) using UV irradiation.
Surface morphology and physico-chemical characteristics of titania nanotube materials play a significant role in the anti-bacterial
activity [221]. Nanostructured AgI/TiO2 photocatalysts have been
developed that showed efficient visible light active photocatalytic
degradation of organic pollutants and photoinduced antibacterial
activity [222]. Visible light active self-cleaning cotton has been fabricated by loading AgI particles on TiO2 functionalized cotton fibers,
which exhibited efficient degradation of methyl orange under visible light irradiation compared to TiO2 -cotton fibers [223]. The
improved visible light activity has been assigned to photoexcitation
of the narrow band AgI, where photogenerated electrons from the
conduction band of AgI can be transferred to the conduction band
of TiO2 , thereby increasing the charge separation along the heterojunction interface. Silver nanoparticles were deposited on the
surface of TiO2 nanoarrays to construct photocatalytic self-cleaning
substrate combined with surface enhanced Raman active detection
platform [224,225].
412
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 23. Proposed mechanism of photocatalytic self-cleaning antimicrobial action.
(Reprinted from Appl. Catal. B: Environ. 130–131 (2013) 8–13 copyright (2013) permission from Elsevier Science).
Several mechanisms have been proposed to account for the
antibacterial activity of TiO2 . Upon illumination of TiO2 with suitable light, several ROS such as hydroxyl radical, hydrogen peroxide,
and superoxides are generated, which can be potentially fatal for
microorganisms (Fig. 23). Irradiation of TiO2 can destroy the cell
wall and cell membrane of bacterial cell [226,227]. Rengifo-Herrera
et al. reported that for N, S co-doped TiO2 , photogenerated holes
generated upon visible light irradiation do not possess suitable
reduction potential to produce • OH radical by the oxidation of H2 O
[228,229]. Under visible light irradiation, less oxidative O2 •– , and
1 O are thought to be responsible for the photocatalytic decompo2
sition of bacterial cells. However, UV light excitation can produce
highly oxidizing • OH radicals, which can cause photocatalytic bacterial inactivation [228,229].
6. Photocatalytic hydrophobic surfaces
Superhydrophobic surfaces are characterised by low free energy
surfaces possessing a WCA greater than 150◦ . The hydrophobic surfaces can be fabricated by controlling the chemical compositions
and geometric structures of solid surfaces. In contrast to superhydrophilic photocatalytic materials, there are very limited examples
of superhydrophobic photocatalytic surfaces [70,230–233]. However, these surfaces offer several advantages as self-cleaning
materials over superhydrophilic surfaces, including reduction in
bacterial adhesion [234], superior cleaning action due to “lotus
effect” [235] and anti-misting property [236]. The examples
provided in this section summarize various strategies such as
functionalization of TiO2 surfaces with PTFE, PDMS, fluorinated
alkyl moieties and modification of surface morphology, which can
increase surface roughness and lower the surface free energy. The
presence of the hydrophobic coatings, in most of the cases, prevents
complete hydrophilic conversion of TiO2 upon irradiation while the
TiO2 surfaces display photocatalytic and hydrophobic properties
simultaneously.
Nakajima et al. developed transparent superhydrophobic films
by calcination of a mixture of aluminium acetylacetonate and
titanium acetylacetonate, followed by coating with a fluoroalkylsilane [237]. The films were characterized by rough, porous surface
and the roughness was correlated to the concentration of TiO2
in the film. The film containing 2 wt% TiO2 showed a WCA 140◦
after illumination with UV light (1.7 mW/cm2 ) for 800 h. The film
maintained its hydrophobicity and exhibited photocatalytic degradation of stains upon exposure to outdoor light for 1800 h. The
self-cleaning action of the superhydrophobic film has been
explained in terms of photocatalytic activity of TiO2 combined
with its photoinduced amphiphilic property (i.e., possessing both
hydrophilic (water-loving) and lipophilic (fat-loving) properties,
simultaneously). Calcium hydroxyapatite (HAP) based photocatalyst has been developed, where Ti(IV) ions partially substitute Ca2+
ions [238]. Ti(IV)-doped HAP particles showed decomposition of
acetaldehyde under UV irradiation. Further coating of Ti(IV)-doped
HAP particles with a fluoroalkyl silane (FAS) and a methacrylate
based hydrophobic organic polymer resulted in a superhydrophobic film with a WCA 155◦ and an oil repellent property [232].
However, the FAS treated Ti(IV)-HAP polymer composite displayed
low photocatalytic efficiency for the degradation of isopropanol,
which presumably resulted from the low surface exposure of Ti(IV)HAP photocatalytic particles and the presence of FAS coating that
prevented diffusion of gaseous contaminants. The FAS treated
Ti(IV)-HAP-polymer composite films maintained their hydrophobic character for a long period of time (>600 h) upon exposure to
exterior light. This probably arises from the presence of FAS coating,
which inhibits direct contact with Ti(IV)-HAP and polymer.
Superhydrophobic nanocomposite coating of TiO2 and polytetrafluoroethylene (PTFE) has been developed using a radio
frequency-magnetron sputtering (RF–MS) deposition method
[239]. The film exhibited UV-light induced photocatalytic degradation of oleic acid and the superhydrophobicity was retained after
five cycles of oleic acid adhesion and UV-illumination (Fig. 24).
Thin film of TiO2 nanoparticles dispersed in polydimethylsiloxane (PDMS) has been synthesized using aerosol assisted chemical
vapor deposition technique [240]. The resultant thin film exhibited superhydrophobic nature (WCA 162◦ ) due to high surface
roughness and low surface energy of the polymer. Additionally,
the film also retained its superhydrophobic character and did not
undergo any significant degradation after prolonged irradiation
with UV light ( = 365 nm). The high surface area of the polymer surface also allows incorporation of a higher concentration of
titania nanoparticles and thus a high rate of photocatalysis. Superhydrophobic coatings were also developed using TiO2 nanowires
and PDMS though simple dipping process [241]. Scanning electron microscopy images showed that the TiO2 nanowires aggregate
in the coating to form dendrite structures, which increase surface
roughness, with WCA 158 ± 2◦ (see Fig. 25a); however, the surface was found to convert into a hydrophilic one (WCA 25◦ ) after
UV illumination for 6 h (8 W Hg lamp, = 254 nm) and also displayed anti-fouling property for low boiling solvents. Following UV
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
413
Fig. 24. (a) Field emission scanning microscopic image of TiO2 /PTFE. (b) Changes in water contact angle on TiO2 /PTFE on Ti substrate on oleic acid and UV illumination.
(Reproduced from Adv. Mater. 24 (2012) 3697–3700, with permission from Wiley).
illumination, the increased value of oxygen/Ti ratio suggested an
increase in the concentration of hydroxyl group [241]. The selfcleaning action of the surface was examined in terms of its ability
to remove graphite powder sprinkled on the surface, which adsorbs
readily on the surface of a water droplet placed on the hydrophobic
surface and can be readily slided off the surface (see Fig. 25b). The
easy fabrication method also allows easy repairability and regeneration of the superhydrophobic surface, which is beneficial to reduce
mechanical damage and useful for applications in self-cleaning
materials.
Multifunctional TiO2 –high-density polyethylene (HDPE)
nanocomposite surface has been fabricated through a template
lamination method [242]. The nanocomposite surface possessed
hierarchical roughness ranging from micro to nanoscale (Fig. 26).
The surface exhibited superhydrophobicity (WCA 158◦ ), low slipoff angle and self-cleaning properties, which were also maintained
in the absence of UV light. Illumination of the photocatalytic
hydrophobic surface with UV light resulted in a hydrophilic
surface due to the oxygen vacancies and the hydrophobicity was
eventually restored by heating, which presumably changes the
surface composition by reversing the UV induced Ti O H bonds
to more hydrophobic Ti O bonds. Superhydrophobic films with
WCA as high as 155.5◦ have been developed using hybrid layers
of TiO2 and dodecylamine [243]. The film retained hydrophobicity for 4 weeks in outdoor applications in the presence of high
relative humidity (>90%). The enhanced hydrophobicity of the
Fig. 25. (a) Changes in WCA of superhydrophobic TiO2 upon UV-illumination, (b) self-cleaning process on a superhydrophobic TiO2 surface.
(Reprinted from Appl. Surf. Sci. 284 (2013) 319–323 with permission from Elsevier).
414
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 26. Schematic illustration of water–air interface on TiO2 –HDPE nanocomposite surface possessing hierarchical structural roughness.
(Reprinted from ACS Appl. Mater. Interfaces 5 (2013) 8915–8924 with permission from American Chemical Society).
inorganic–organic hybrid films was attributed to the outward
orientation of hydrocarbon chains in the hybrid film.
7. Reversible photo-controlled wetting
Reversible photo-response surfaces with controlled wetting
properties have attracted significant attention due to its application in surface engineering of ceramic and bio-materials [244–248].
These tuneable ‘smart coatings’ can switch reversibly between
hydrophilic and hydrophobic surfaces by irradiating with light
of appropriate wavelength [248]. The unique properties of these
materials have applications in a number of technological areas
such as sensors, controlled drug delivery and smart membranes
or coatings [248–251]. Most important factors in controlling the
reversible nature of wetting are surface roughness, morphology,
and the polarity of the surface [244,247,252,253]. Li et al. reported
Fig. 27. Schematic representation of the reversible photo-controlled wetting of TiO2 –SiO2 composites under UV irradiation.
(Reproduced from Appl. Surf. Sci. 283 (2013) 12–18 with permission from Elsevier).
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
415
Fig. 28. Origin of underwater superoleophobicity due to formation of thin film of water between an oil drop and TiO2 surface.
(Reprinted from Langmuir 29 (2013) 6784–6789, with permission from American Chemical Society).
Fig. 29. Oil–water separating device based on titanium mesh, n-hexadecane dyed with Sudan IV (red) and water dyed with methylene blue (blue) were used as oil and water
phases, respectively. (For interpretation of the references to color in this figure legend, the reader is referred to the web version of this article.)
(Reprinted from Langmuir 29 (2013) 6784–6789 with permission from American Chemical Society).
the preparation of a novel micro-nano hierarchical titania/silica
composite thin-film by modifying the microspheres of SiO2 with
nano-spheres of TiO2 and a commercial water-resistant agent
(Aquapel), as shown in Fig. 27. These ordered TiO2 –SiO2 composites exhibited diverse degrees of amplified wettability [248].
It was also showed that the water contact angle is significantly
reliant on the microscopic surface roughness [248]. The effect of
TiO2 –SiO2 size ratio on the wetting properties of these composites
were described using the Cassie-Baxter equation [248]. It should
also be noted that Mills et al. have indicated that photo-induced
superhydrophilicity may be due to the surface restructuring of an
intrinsically hydrophobic titania surface during the irradiation process [254].
8. Underwater-superoleophobicity
In recent years, materials that exhibit underwater superoleophobicity have received significant attention due to their
applications in marine antifouling, oil spill clean-up, water management etc. [26,255]. Photoinduced underwater superhydrophobicity
of TiO2 surfaces has been reported for TiO2 thin films prepared
by sol–gel process, coated on a glass slide or synthesized by
calcination of a Ti plate at 500 ◦ C [256]. UV irradiation resulted
in a highly amphiphilic TiO2 surface demonstrating underwater
superoleophobicity with an oil contact angle (OCA) higher than
160◦ . The photoinduced underwater superoleophobicity results
from the presence of a thin water film formed from the trapped
water molecules on the surface (Fig. 28), which in turn inhibits
the contact between oil droplets and TiO2 surface. TiO2 surface
was found to lose its superwetting property upon contamination
treatment, which was recovered after UV-irradiation and the wettability conversion was reversible for at least three cycles. An
oil/water-separating device (Fig. 29) has been designed containing
TiO2 surface on a titanium mesh with a pore size of approximately
150 m, which exhibited an efficient separation of oil (treated with
a red dye Sudan IV) and water (dyed using methylene blue as the
blue dye).
An underwater superoleophobic coating derived from flower
like rutile TiO2 grown on fluorine doped tin-oxide (FTO) substrate
has been reported recently [257]. The coatings exhibited superamphiphilicity in an air–solid–liquid three-phase system, with both
WCA and OCA values of 0◦ , which results from the hydrophilicity of TiO2 combined with the hierarchical flower like structure
of the coatings. The coatings showed an oil-repellent property
416
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 30. Schematic illustration showing the fabrication of SWCNT/TiO2 nanocomposite and its application in separation of oil in water emulsion.
(Reproduced from ACS Nano 8 (2014) 6344–6352, with permission from American Chemical Society).
similar to fish scales with an underwater OCA 155◦ , which presumably results from the presence of water molecules trapped
in the cavities of rough TiO2 surface thus resulting in a repulsive
interaction between water and oil molecules. In the presence of
contaminants, superwetting state of the coating decreased, resulting in an increase in WCA from 0◦ to 137◦ and decrease in OCA
from 155◦ to 64◦ . However, the superamphiphilicity and underwater superoleophobic property of the film recovered upon irradiation
with UV light for 2 h and the reversible transition between underwater oleophilicity and underwater superoleophobicity could be
performed for several cycles without any loss in response by changing between contaminant treatment and UV exposure [257]. An
ultrathin film made of single-walled carbon nanotubes (SWCNTs)
and TiO2 nanocomposites has been fabricated that demonstrated
superhydrophlicity, superoleophilicity, and underwater superoleophobicity upon UV-illumination (Fig. 30) [258]. The UV-illuminated
film exhibited underwater contact angles higher than 150◦ for
different oils, which result from the extremely low oil-adhesion
force of the UV-irradiated film. The SWCNT network provides
nanoscale thick and porous (20–60 nm pore size) structure that
enables efficient and ultrafast separation of both surfactant free
and surfactant-stabilized oil-in-water emulsions compared to
commercial filtration membranes. Moreover, the UV-induced photocatalytic activity of TiO2 imparts additional antifouling property
to the SWCNT/TiO2 thin films, which is beneficial for the repeated
and long-term use of the filtration membranes. Superhydrophobic
and underwater superoleophilic membranes composed of sulfonated graphene oxide (SGO) nanosheets and nanostructured TiO2
spheres have been fabricated for efficient separation of surfactant
stabilized oil in water emulsion [259]. The crosslinked nanostructured networks of SGO/TiO2 membrane provide mechanical
flexibility and allow high oil rejection rate combined with very low
membrane fouling.
Fig. 31. Schematic diagram showing the bio-inspired SnO2 films causing degradation of organic dyes and pathogen.
(Reproduced from Nanoscale 5 (2013) 3447–3456 with permission from Royal Society of Chemistry).
9. Other material displaying self-cleaning activity
Though TiO2 based photocatalytic materials have received most
attention for developing self-cleaning materials, other n-type metal
oxides such as ZnO and SnO2 , also exhibit both photocatalytic activity and photoinduced hydrophilic conversion [77]. SnO2 nanorods
displayed switchable superhydrophobicity (WCA 154.1◦ ) before UV
exposure and superhydrophilicity (WCA 0◦ ) upon UV irradiation
[260]. The hydrophilic conversion has been attributed to surface
roughness, formation of oxygen vacancies and surface hydroxyl
groups upon UV illumination. Deposition of bio-inspired SnO2 films
on glass surface has been achieved by functionalization with spermine [261]. The bio-inspired SnO2 films generated superoxide
radicals (• O2 − ) upon exposure to sunlight and caused degradation
of organic dyes and pathogens (Fig. 31).
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
417
Fig. 32. Heterojunction formation of ZnO with BiVO4 .
(Reproduced from Ind. Eng. Chem. Res. 53 (2014) 8346–8356 with permission from American Chemical Society).
The photocatalytic activity combined with the photoinduced
hydrophilicity of SnO2 films can be applied to develop coatings with
antifouling properties. Pan et al. reported the fabrication of SnO2
nanowire based heterostructures that exhibit hydrophobicity due
to rough morphology of the surface [262]. The grooves present in
the surface microstructure allow trapping of air and prevent penetration of water molecules. These heterostructures demonstrated
switchable wettability changes upon alternating exposure to UV
illumination, storage in dark and O2 annealing, which can be beneficial to develop industrial coatings for self-cleaning applications.
Sun et al. demonstrated that thin films of ZnO show a WCA
of 109◦ before UV irradiation and their surfaces are converted to
highly hydrophilic upon UV exposure [263]. The photoinduced
hydrophilic conversion has been attributed to the formation of
surface defects similar to TiO2 upon UV exposure and subsequent adsorption of water molecules to the defect sites. Plasmon
assisted visible light absorbing Ag–ZnO hybrids have been fabricated that exhibit surface enhanced Raman scattering (SERS)
and enhanced photocatalytic activity due to efficient separation of
charge carriers along the hybrid structure [264]. These UV–visible
light induced photocatalytic and uniform SERS active nanoarrays can potentially be used for self-cleaning applications. Guo
et al. reported the fabrication of superhydrophobic self-cleaning
ZnO/CuO heterohierarchical nanotrees after silinazation [265].
The superhydrophobicity was attributed to the surface roughness and presence of trapped air in the rough surface cavities.
Heterojunction formed using ZnO and BiVO4 showed enhanced visible light absorption and superior photocatalytic degradation of
organic dyes compared to pure ZnO [266]. The improved activity
of the heterojunction results from reduced rate of electron–hole
recombination and enhanced visible light absorption (Fig. 32). The
heterojunction showed hydrophobic surface (WCA 112.5◦ ) after
treatment with tetraorthosilicate (TEOS), which can be useful to
design self-cleaning materials.
Kako et al. demonstrated the photoinduced hydrophilic and
lipophilic property of InNbO4 thin films [267]. The number of
polar groups (e.g., hydroxyl group) was found to increase in the
presence of UV irradiation and the mechanism of photoinduced
amphiphilicity was thought to be similar to that of TiO2 . Unilamellar nanosheets of TiNbO5 , Ti2 NbO7 , Ti5 NbO14 , and Nb3 O8
were evaluated for their photocatalytic activity and photoinduced
hydrophilicity [268]. Nanosheets of Nb3 O8 exhibited higher thermal stability and efficient photoinduced hydrophilicity compared
to polycrystalline anatase TiO2 . The high stability of Nb3 O8 photocatalysts at elevated temperature is advantageous for applications
in building materials, which require high processing temperatures.
10. Testing methods for photocatalytic self cleaning
surfaces
Measurement of contact angle and photocatalytic degradation
of organic dyes are commonly used to evaluate the self-cleaning
activity of photocatalytic surfaces [254]. International standard
methods have been developed to determine the efficiency of selfcleaning, which can be used by manufactures to characterize their
products and ensure quality and reliability.
10.1. ISO 27448: 2009: Standard testing method for
photocatalytic self-cleaning surfaces by measuring the contact
angle
An international standard organization (ISO) testing method
(ISO 27448: 2009) has been published to determine the efficiency
418
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 33. Typical data generated for contact angle, , vs. irradiation time, in the standard ISO 27448: 2009.
(Reproduced from J. Photochem. Photobiol. A 237 (2012) 7–23, with permission
from Elsevier).
of self-cleaning of photocatalytic surfaces, which relies on the measurement of WCA upon UV illumination [269]. The method involves
application of an organic compound (usually oleic acid, C18 H34 O2 )
on the photocatalytic surface and the wettability of the surface is
subsequently monitored by measuring the WCA as a function of UVirradiation time. The oleic acid can be applied either manually or by
employing a dipping process. In the manual coating process, 200 l
C18 H34 O2 is dropped onto the middle of an initially weighed sample. The dropped C18 H34 O2 should be evenly spread by employing a
non-woven cloth. Excess C18 H34 O2 should be wiped off so that the
total weight of the C18 H34 O2 becomes 20 g cm−2 , as measured by
weighing the coated sample. For the dipping process, the sample is
placed in a 0.5% v/v solution of C18 H34 O2 in n-hexane. These coated
samples should then be dried in an oven set at 70 ◦ C for 15 min. The
measurement is continued until the WCA reaches a value less than
5◦ (Fig. 33). Carbon dioxide and water will be formed after the photocatalytic mineralization of oleic acid in the presence of oxygen
and light irradiation (Eq. (11)).
Photocatalyst
hϑ ≥ 3.2eV
C18 H34 O2 +25.5 O2 −−−−−−−−−−−→18CO2 +17H2 O
(11)
Before carrying out the measurements, the surface should be
irradiated for at least 24 h under UV irradiation (for manual coating recommended irradiance dose is 2 mW/cm2 while the dipped
samples should be irradiated with 1 mW cm−2 of UVA) to remove
organic contaminants and should be handled with proper care to
avoid any further contamination. It is also recommended that the
initial contact angle should be higher that 20◦ to observe the change
upon UV irradiation and measurements should be performed at
five different points in order to obtain an accurate average contact angle. The method provides an easy and effective measure to
determine the self-cleaning efficiency of photocatalytic materials;
however, it does not incorporate extremely hydrophobic surfaces,
granular and water permeable substrates and visible light active
photocatalysts. The advantage of this test is that it provides a quick
and easy method to identify the photocatalytic self-cleaning action.
The major disadvantage of this method is that the conditions for
carrying out the testing procedures (e.g., operating temperature
and humidity) are not well defined [254] and the contact angle
measurements can vary significantly with different experimental
conditions. It is also not reported why two different coating procedures are suggested and why two different UVA irradiance dose
should be employed for the two differently coated samples [254].
10.2. ISO 10678; 2010, ‘Determination of photocatalytic activity
of surfaces in an aqueous medium by degradation of methylene
blue’
A UV/visible spectrophotometric method (ISO 10678; 2010)
has been developed utilizing the photo-induced bleaching of
methylene blue (MB) dye to assess the activity of photocatalytic
self-cleaning materials [270]. The high molar extinction coefficient
of MB (C16 H18 N3 SCl) allows monitoring the photocatalytic process
conveniently through a striking color change of the dye from blue
to colorless due to photo-mineralization (Eq. (12)). C16 H18 N3 SCl
can completely be mineralized into simple molecules such as HCl,
H2 SO4 , HNO3 , CO2 and H2 O through a series of photocatalytic
degradation process [271]. However, these photo-assisted degradation reactions take place on a much larger timescale than the
oxidative photo-bleaching of C16 H18 N3 SCl. It should therefore be
noted that the rate of photo-bleaching of C16 H18 N3 SCl is not equal
to that of the mineralization of the dye.
Photocatalyst
hϑ ≥ 3.2eV
C16 H18 SCI+25.5O2 +−−−−−−−−−−−→HCl+H2 SO4 + 3HNO3
+ 16CO2 +6H2 O
Fig. 34. Set up for the photocatalytic degradation studies of methylene blue.
(Reproduced from Energy Environ. Sci. 5 (2012) 7491–7507 with permission from Royal Society of Chemistry).
(12)
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
419
The experimental setup (Fig. 34) involves fixing a glass cylinder
on a sample plate (typically 10 cm2 ) containing the photocatalytic
coating. During the preconditioning step, ca. 35 mL MB (20 M) is
added to the cylinder and covered with a UV-A transparent glass
plate for 12 h in dark to ensure adsorption of dye on the surface.
This is followed by irradiation with UV-A light (recommended dose
1.0 mW/cm2 ) with occasional agitation of the solution at every
20 min. The photocatalytic process is monitored through decomposition of MB by measuring absorbance of the solution at 665 nm
spectrophotometrically. From the known values of rate of photocatalytic bleaching of MB (r), the UV-A irradiance, photonic efficiency
() for a photocatalytic sample can be calculated according to the
following equation.
=
100 × r
IUV
(13)
Photocatalyzed decomposition of MB provides a simple and
convenient measure of the activity of photocatalytic self-cleaning
materials; however, varying purity of commercially available MB
often affect the molar extinction coefficient and therefore results
in errors in preparing dye solution of a specific concentration. It
should be mentioned that in addition to photocatalytic decomposition, photobleaching of MB can also occur through a dye
sensitization mechanism, during which an electronically excited
dye molecule (D*) injects an electron to the conduction band of
the semiconductor and gets converted to radical cation (D•+ ). The
dye radical cation can in turn undergo decomposition resulting in
photobleaching. This dye sensitization mechanism can be avoided
by choosing proper excitation source, (excitation = 365 nm), where
MB does not absorbs significantly. The non-catalytic dye-sensitized
reaction can be minimized by controlling the pH of the solution
at 5.5 (lower than the point of zero charge of the semiconductor
ca 6.6 for TiO2 ), which ensures minimal dye adsorption and thus
lowers the extent of dye sensitized photobleaching reaction. MB
decomposition test provides reliable results for moderately active
materials such as commercial self-cleaning glass; however, the low
diffusion coefficient of the dye limits its use in evaluating the highly
active materials [254,272]. Additionally, due to lower photostability of MB, this method is not very effective in assessing low activity
materials such as commercial photocatalytic tiles [272].
The advantage of ISO 10678; 2010 is the simplicity of the experimental set up. The major disadvantage is that the purity of the
C16 H18 N3 SCl is not defined in the standard and as noted by Mills
et al. the high variation in the purity of commercially supplied
C16 H18 N3 SCl means that it may not be possible to prepare a 10−5 M
concentration of methylene blue with confidence [254]. It was previously noted that the methylene blue test is more appropriate as
a water-purification test than a self-cleaning test [254].
Fig. 35. Experimental set up for sample irradiation (1) UV light source, (2) metal
plate (for irradiation level adjustments), (3) lid, (4) petri dish, (5) adhesive film, (6)
test samples with inoculated bacteria (7) U-shaped glass rod or tube and (8) moist
filter paper.
(Reproduced from J. Photochem. Photobiol. A 237 (2012) 7–23 with permission from
Elsevier).
10.3. ISO 27447: 2009, ‘Fine ceramics, advanced technical
ceramics – test method for antibacterial activity of
semiconducting photocatalytic materials’
R = log(BL /C L )–log(BD /C D )
ISO 27447: 2009 defines a testing process for the antibacterial
activity of photocatalytic materials or films on the surface (Fig. 35),
by evaluating the enumeration of bacteria under UV irradiation
[273]. This protocol is usually used for photocatalytic materials
coated on construction supplies (such as boards, flat sheets or
plates) or antimicrobial fabrics. ISO 27447: 2009 method does not
include powder, granules or porous ceramics. There are two major
procedures employed in this analysis: (i) film adhesion, and (ii)
glass adhesion. The former method is recommended for the analysis
of flat surfaces while the latter method is designed for the assessment of fabric materials. For the film adhesion method bacteria
such as S. aureus and E. coli are the recommended bacteria employed
in the test while the glass adhesion method recommends the use
of S. aureus and Klebsiella pneumoniae [55,254]. It should be noted
that ISO 27447: 2009 is specifically designed for testing surfaces
and does not deal with the photocatalytic disinfection of water or
air.
In the film adhesion method, the bacterial strains (e.g., S. aureus
and E. coli) are inoculated into the nutrient agar and then subjected
to incubation at a temperature of 37 ◦ C up to 24 h. The bacteria are
then moved to a new agar medium and incubated for another 24 h. A
portion of these bacteria is then transferred to a diluted form of the
nutrient broth (1/500 NB) and then bacteria are counted using an
optical microscope. The bacterial suspension is then diluted with
1/500 NB to get a concentration of 6.7 × 105 –2.6 × 106 cells ml−1
[273]. This sample will then be inoculated on the surface of the
material to be tested [254]. The photocatalytic anti-microbial action
(RL ) after 8 h of UV treatment with light irradiance L mW cm−2 , can
be written as:
RL = log(BL /C L )(14)
where CL and BL are the number of live bacteria after the illumination period for photocatalytic samples and non-photocatalytic
specimens, respectively. Dark control materials with and without
the photocatalyst coating should also be developed and kept under
the dark condition for 8 h. Live bacteria counts on the specimens
with and without the photocatalyst coating after 8 h under the dark
conditions are then analysed as: BD and CD . The overall photocatalytic antibacterial action R, can be calculated as:
(15)
This is a well-defined and the best available standard to date for
benchmarking the commercial photocatalyst based anti-bacterial
products. However, the main disadvantage is the recommendation
to use two different methods for flat surfaces and fabrics. It is also
not fully clear why different strains of bacteria are recommended
for these two methods [254,274].
10.4. Photocatalytic activity indicator inks
Most of the ISO standard methods developed until today require
expensive analytical instrumentation, skilled personnel, and long
analysing time. Recently photocatalytic activity indicator inks have
been developed that utilize various redox dyes such as resazurin
(Rz), basic blue 66 (BB66) and acid violet 7(AV7) to evaluate the
photocatalytic activities of a broad range of materials such as
420
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Fig. 36. Photocatalytic activity indicator tests for probing glass, paint and tile surfaces.
(Reproduced from J. Photochem. Photobiol. A 290 (2014) 63–71 with permission from Elsevier).
Fig. 37. Structures of resazurin (Rz) and resorufin (Rf).
commercial paints, tiles and glasses (Fig. 36) with varying activities
[275–278].
The photocatalytic activity indicator ink consists of a redox
dye (D) and a sacrificial electron donor (SED) such as glycerol.
Both the dye and the SED are incorporated in a suitable polymer
such as hydroxyl ethyl cellulose and applied onto the semiconductor (SC) surface. The working mechanism of the ink involves
a photo-reduction reaction, where the photocatalytic surface upon
illumination generates an electron and hole pair. The photogenerated electrons reduce the dye resulting in a color change of the
indicator ink [279]. For example, the reaction mechanism of testing
using dye molecules such as resazurin (Rz) can be described as follows in Eqs. (16)–(18). The system consists of a dye (in this case it is
Rz), a sacrificial electron donor or SED (e.g., glycerol) and a polymer
material (for example, hydroxyl ethyl cellulose (HEC)), to perform
as an encapsulating agent for Rz and SED.
The reaction follows through a photo-reduction pathway as
described by reactions 16–18.
hv E g
−
TiO2 → TiO2 ∗ h+
vb , eCB
(16)
−
−
SED+TiO2 ∗ h+
vb , eCB → SEDox + TiO2 ∗ eCB
+ 2H+ → Rf + H2 O
Rz + e−
CB
Fig. 38. The tools employed to carry out the photocatalytic activity indicator ink.
(J. Photochem. Photobiol. A 272 (2013) 18–20. Reproduced with permission from
Elsevier).
(17)
(18)
Illumination of the surface coated with a semiconductor such as
TiO2 with a light having energy of excitation higher than the bandgap energy (Eg ) of the semiconductor, facilitates photoexcitation of
valence band electron to the conduction band resulting a positive
electron hole (h+ VB ) in the valence band. Rz, which is blue coloured,
can accept the conduction band electron (e− CB ) and gets reduced
to a pink coloured resorufin (Rf) during this reaction (Fig. 37).
The time required for the change from blue to pink or the
overall rate of color change gives a measure of the self-cleaning
photocatalysis. The details and conditions required for this test
are comprehensively explained in previous publications [275–277].
The tools employed to carry out this ink test include Rz dye, a wire
wound rod (K-bar) and a scanner (Fig. 38)
The photocatalytic activity of a material can be evaluated by
monitoring the color change of the indicator ink as a function of
irradiation time. Semi-quantitative information can be obtained by
recording the digital images of the color changes using a hand-held
scanner and analyzing the changes in red–blue–green components
as a function of time using an image analysis software (Fig. 39).
This testing method provides an inexpensive and quick measure to
probe photocatalytic materials with varying activities and is therefore highly beneficial for both researchers and manufacturers to
rapidly screen activities of new materials.
Unlike the previously discussed ISO test protocols, these dye
based characterization are inexpensive, simple and quick (typically
<10 min) [276]. These dye testing results correlate well with tests
such as the self-cleaning activity measurements using stearic acid.
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
421
Fig. 39. Self-cleaning test using photocatalytic activity indicator ink (a) test results recorded at 30 s irradiation intervals for self-cleaning glass (top) and, plain glass (bottom).
(b) A plot of variation of the RGB (red) with irradiation time, extracted from the images. (For interpretation of the references to color in this figure legend, the reader is
referred to the web version of this article.)
(J. Photochem. Photobiol. A 272 (2013) 18–20. Reproduced with permission from Elsevier).
The round robin test on various surfaces showed that their average
repeatability and reproducibility are around 11% and 21%, respectively. These test protocols have significant potential to grow in the
area of rapid quality control for the photocatalytic industries [276].
11. Commercial applications of photocatalytic self cleaning
surfaces
The photoinduced hydrophilic conversion of TiO2 surface has
been exploited commercially to develop anti-fogging, self-cleaning
Fig. 40. Schematic illustration of the working mechanism of self-cleaning glasses (from left to right), which require: accumulation of pollutants on glass, activation of the
photocatalytic coating by UV light, photocatalytic degradation of the organic pollutants and finally washing the decomposed materials by rain water.
(Reproduced from Sol. Energy Mater. Sol. Cells 109 (2013) 126–141 with permission from Elsevier).
422
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
Table 3
Uses of self-cleaning materials.
Substrate
Application
Reference
Glass
Mirrors for vehicles and indoor
uses, windows, tunnel, road lights
and vehicles
Kitchen, bathroom, building roof,
and walls
Hospital garments, medical
devices, house hold appliances,
interior furnishing and protective
clothing
Automotive industry and buildings
[4–8], [192]
Tile
Textile/fiber/cotton
Plastic/polycarbonate
[9,10]
[1–3]
[3,195]
surfaces for various applications such as fabrics, paints, glass, tiles
and cement. A brief summary of use of self-cleaning materials is
presented in Table 3.
Modification of tiles and glass windows using transparent TiO2
photocatalysts thin films has been used to construct building materials with photocatalytic self-cleaning properties [280–284]. The
self-cleaning action can be achieved by activating the photocatalysis process utilizing solar irradiation as illustrated in Fig. 40. ActivTM
developed by Pilkington glass represents the first example of selfcleaning glass, consisting of a 15 nm thick nanocrystalline TiO2
film deposited on a glass surface [285]. ActivTM represents one of
the most successful self-cleaning products and is currently used in
various commercial and private buildings world-wide. The suitability of ActivTM as a reference for semiconductor film photocatalysis
has been investigated by Mills et al. [9]. The photocatalytic activity
of ActivTM was measured in terms of its ability to degrade stearic
acid. The suitability of ActivTM as a photocatalytic reference material results from its high mechanical endurance and reproducible
photocatalytic activity. Additionally, low visible reflectance ( 7%),
favorable absorption of solar radiation, and transmittance properties of ActivTM are also useful for the self-cleaning applications. In
recent years, several other self-cleaning glasses such as Radiance
TiTM , SuncleanTM , and BiocleanTM are also coming into commercial
applications.
The Japanese company TOTO Ltd., introduced a photoinduced
superhydrophilicity based technology, HydrotechTM , which uses
sunlight to break down pollutants that can be washed away
with rain/water. HydrotechTM has been successfully applied in
building materials, coatings and paints made by TOTO Ltd., for
indoor and outdoor applications. The photocatalytic products are
manufactured by spraying a liquid suspension of TiO2 on the
surface. The surfaces are subsequently sintered at 600–800 ◦ C
to strongly attach the TiO2 layer on the surfaces [286]. Commercial applications of photocatalytic TiO2 -coated materials in
the fabrication of self-cleaning glazing products require high
processing temperatures; hence, high-temperature stability of
photocatalytically active anatase TiO2 is highly desirable. Nonmetallic doping has been reported to increase the thermal stability
of anatase phase [287,288], however, this can also promote
electron–hole recombination and reduced photocatalytic activity.
Recently, visible-light-active, oxygen-rich TiO2 has been developed
in which anatase phase is stable up to 900 ◦ C [289]. High thermal
stability of anatase–TiO2 can be useful for developing self-cleaning
building materials.
Recently, it was shown that an ethenol suspension of perfluorooctyltriethoxysilane (C14 H19 F13 O3 Si) coated anatase TiO2
nanoparticles produced a paint that can be coated or extruded onto
both hard and soft materials to create a self-cleaning surface. These
superhydrophobic coatings can be applied on clothes, paper, glass,
and steel for numerous self-cleaning applications. As it is described
in Fig. 41, water droplets bounce off from the surface without wetting the material [290].
Fig. 41. Time-lapse images of water-drops bouncing on the self-cleaning glass, steel,
cotton, and paper surfaces.
(Reproduced with permission from Science 347 (2015) 1132–1135).
Fig. 42. Self-cleaning cement coated on (A) Dives in Misericordia Church in Rome
(Reprinted Appl. Catal. B 170–171 (2015) 90–123 with permission from Elsevier
Science). (B) Roof of Dubai Sports City’s Cricket Stadium. (Reproduced from Energy
Environ. Sci. 5 (2012) 7491–7507 with permission from Royal Society of Chemistry).
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
423
Fig. 43. Automotive mirror, left: uncoated, right: coated with TiO2 .
(Reproduced from Energy Environ. Sci. 5 (2012) 7491–7507 with permission from Royal Society of Chemistry).
Self-cleaning glass coated with TiO2 nanoparticles has been
applied on the surface of National Opera Hall, China [291]. TiO2
nanoparticles containing white cement has also been used in Dives
in Misericordia Church in Rome [292] and Roof of Dubai Sports
City’s Cricket Stadium (Fig. 42). The Italian multinational company, Italcementi is very active in the research and development
of self-cleaning cements and has developed a range of photocatalytic cements and are commercially available in the form of TX
AriaTM , TX ActiveTM , and TX ArcaTM [293]. It has been reported
that covering 15% of urban surfaces of the city of Milan with concrete containing TX Active® would reduce the pollution up to 50%
[293]. TioCemTM , supplied by Heidelberg Cement Technology Center, GmbH, is another popular self-cleaning photocatalytic cement
product available in the market to reduce air pollution [294,295].
Eco-friendly, self-cleaning windows and roof tiles are widely
used in Japan. Self-cleaning coatings with antifogging properties
have been used in automotive industry to develop clean and glare
free windows, automotive mirrors (Fig. 43), headlights, and mirrors [296]. Water droplets tend to form a continuous film on a
superhydrophilic surface, which in turn eliminates scattering of
light resulting from the presence of condensed water droplets and
thus provides clear and unhindered view. In order to obtain visible
light active self-cleaning building materials, TiO2 thin films were
developed using Ni2+ and Fe3+ dopants [297]. Addition of dopant
metal ions into TiO2 lattice creates intrinsic defects such as oxygen vacancies or Ti interstitial depending on the valence state of
the dopant, which accounts for the visible light absorption. Visible light active glazed ceramic tiles were fabricated by coating the
surface with Degussa P25–TiO2 nanoparticles modified with TEOS
[298]. The modified tiles exhibited higher photocatalytic activity
and improved hydrophilicity under visible light irradiation. The
improved photocatalytic activity and hydrophilicity of the TEOS
modified TiO2 nanoparticles results from the smaller particle size,
larger surface area and increased surface roughness.
Photoinduced antimicrobial action of TiO2 has huge potential
in construction of building materials for both indoor and outdoor
applications [299,300]. Antimicrobial activity of TiO2 is extremely
important for applications in the medical field as well as in food
industries to prevent microbial contamination. Several companies
including TOTO, Karpery and Biocera, have manufactured ceramics
with a deposited thin film of semiconductor photocatalysts functioning as an antimicrobial agent [301]. The resulting products
display photoinduced antimicrobial and deodorizing properties.
In recent time, several reviews have been published on functionalization of textile and wool with TiO2 nanoparticles and their
self-cleaning properties [302,303]; hence a brief summary of the
recent developments is discussed in the current review. Photocatalytic and self-cleaning textile fibers have been designed based
on cotton, polyester, polyamide, cellulose fibers coated with TiO2
NPs [304–307]. Functionalization of textile fibers with TiO2 is usually achieved using carboxylic acid as the anchoring group, which
can coordinate to the Ti atom and can also bind to TiO2 through
H-bonding with lattice oxygen or surface hydroxyl group [302].
Addition of nanocrystalline TiO2 also contributes to the UV protection factor of the fabric, which was found to be preserved
after several cycles of home-washing [308,309]. The TiO2 coating
was found to improve the mechanical properties of cotton fibers
[310] and the coated fibers demonstrated high stain removal and
antibacterial properties [308,309]. Photocatalytic and self-cleaning
cotton fabrics were designed by treating the cotton fibers with
TiO2 nanoparticles and multi-wall carbon nanotubes (MWCNTs)
using succinic acid as a crosslinking agent [311]. The simultaneous coating with TiO2 and MWCNTs significantly improved the
photocatalytic activity of the cotton fiber under both UV and
Fig. 44. Removal of wine stains from cotton textiles coated with TiO2 –SiO2 after irradiating for 0, 4, 8 and 24 h.
(Reprinted from J. Mol. Catal. A 244 (2006) 160–167 permission from Elsevier Science).
424
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
sunlight, which has been assigned to the enhanced light absorption
by the TiO2 –MWCNT composites and reduced rate of electron–hole
recombination. The coating with TiO2 –MWCNT also improved the
abrasion resistance and UV blocking capability of the cotton fibers.
Development of the self-cleaning textiles coated with hydrophilic
TiO2 surfaces has also been reported by Bozzi et al. [312,313]. Radio
frequency plasma and UV-C irradiation have been employed to
introduce oxygenated polar functional groups. These functional
groups facilitated the effective adhesion of metal oxides on the
textile/fabric surface. The self-cleaning activity (Fig. 44) of the
TiO2 –SiO2 -coated fabrics was analyzed by the decolorization of red
wine stains [313]. Pakdel et al. also developed a similar strategy and
it was observed that textiles coated with TiO2 /SiO2 (30:70) showed
the optimum efficiency in stain removal [202]. After a detailed web
search, no manufacturers could be identified for the commercial
supply of photocatalytic fabrics.
Visible light active self-cleaning cottons have been designed
by coating cotton fibers with TiO2 -noble metal composites
[204,314,315]. Wool fabrics coated with TiO2 –Ag nanocomposites
using citric acid as a cross linking agent demonstrated improved
photocatalytic efficiency for the degradation of methylene blue and
saffron stain removal [316]. The combined treatment of polyester
fabric with TiO2 nanoparticles and colloidal Ag nanoparticles also
showed improved UV protective properties and higher antimicrobial and self-cleaning action [317]. Polyester fabrics coated
with AgI/AgCl/TiO2 nanocomposites exhibited high efficiency for
the photochemical destruction of methylene blue and antimicrobial properties against E. coli [318]. The superior self-cleaning
activity resulting from the combination of superhydrophobic
surface with photocatalytic activity of TiO2 was recently demonstrated by TiO2 /TCPP functionalized cotton fabrics coated with
trimethoxy(octadecyl) silane (OTMS) [319]. The functionalized cotton fabrics displayed a superhydrophobic surface induced by the
presence of TiO2 and (OTMS) with a WCA of 156◦ and caused degradation of methylene blue upon visible light illumination.
Keratin base fibrous materials are used in a wide range of
applications including textiles, tires, insulation due to high durability, insulating ability and biodegradability. Photocatalytic and
self-cleaning keratin wool fibers were developed by depositing
nanocrystalline anatase TiO2 [320,321].
CristalACTiVTM is a commercial paint based on semiconductor photocatalysis technology and was developed as a solution to
remove NOx. These materials showed the ability to eliminate up
to 0.5 g/m2 /day of NOx [322]. StoClimasan-ColorTM (active interior paint) incorporated a semiconductor photocatalyst which can
constantly degrade organic pollutants including carbon monoxide
under the influence of light [323]. In an investigation to analyze
the by-products formed during the photocatalytic reaction Auvinen et al. indicated that, if the photocatalytic mineralization is not
fully completed, the end products are not always water and carbon
dioxide. They have examined six different paint products to understand the by-products produced by photocatalytic paints during the
decomposition of formaldehyde, and a mixture of volatile organic
compound (VOC) containing five different indoor air pollutants
[324]. This investigation showed that a number of by-products
including acetone and acetaldehyde were formed during the photocatalytic reaction. It can therefore be concluded that the incomplete
photocatalytic decomposition of indoor pollutants could result in
a number of side products, which could be more harmful than the
pollutants themselves [324].
The huge potential of TiO2 based photocatalytic and selfcleaning materials, as discussed above, can be realized through
rational designing of photocatalyst to utilize solar and indoor irradiation.
12. Conclusions
The article aims to give an overview on photocatalytic selfcleaning materials derived from TiO2 with tunable wettability
properties. These materials constitute an important area of
research in materials chemistry that is experiencing vast growth
in recent years. These photocatalytic self-cleaning materials can
be used in many applications including antibacterial, antifogging, antireflective coatings and can provide a solution to the
growing problem of environmental pollution. Various models
were postulated to understand the mechanism for photoinduced
hydrophilicity. The widely accepted mechanism relies on the formation of surface defects upon UV light illumination [7]. UV
irradiation results in a structural change at the TiO2 surface and as a
result it induces an interfacial force along the solid–liquid boundary
and subsequently the contact angle changes. It was also described
that UV irradiation generates ‘oxygen vacancies’ and thereby Ti4+
ions will be converted to Ti3+ . These ‘oxygen vacancies’ will increase
the affinity for water molecules.
In another theory, it was proposed that UV illumination results
in the reconstruction of hydroxyl groups at the surface [64]. The
extent of hydrophilic conversion is linked to the density of surface
hydroxyl groups. In addition, the positive hole created by the UV
irradiation can diffuse in to the surface of the photocatalyst and gets
trapped at lattice oxygen. As a result, the binding energy between
the Ti and lattice oxygen becomes fragile and water molecules can
break this bond and form new hydroxyl bonds. In another study, it
was proposed that the thermal energy formed as a result of the irradiation can cause desorption of the weakly attached molecules from
the surface of TiO2 [74]. It is therefore evident that no consensus has
been reached so far in explaining the exact mechanism of photoinduced hydrophilicity and a combination of various mechanism is
often required to account for the phenomenon.
Reversible photo-controlled materials with tunable wetting
properties have recently attracted significant attention due to
their technological application. Surface roughness, morphology,
and the polarity of the surface are reported as the significant
factors in controlling the reversible nature of the wetting. A
number of methodologies such as doping with metals or nonmetals, fabrication of semiconductor nano-composites, formation
of hetero-junctions etc. were reported to improve the selfcleaning activity by the photocatalytic action. However, it has
been noted that it is often difficult to compare the self-cleaning
activity of various photocatalysts due to variation in the nature
of irradiation, intensity of the light employed, time for irradiation etc. In general, any modifications which could increase
the surface roughness by chemical treatments (e.g., doping or
surface treatments) would be a promising strategy to increase
the self-cleaning activity of the materials. Development of heterostructure of the photocatalysts with other materials to increase
the charge separation appeared another effective approach to
improve the self-cleaning efficiency. However, further investigations are required to understand structure activity relationships
and excited state behavior of the photocatalysts, which will be
crucial for designing novel TiO2 -based functional material with
improved photoreactivity and wettability character. Moreover, current research mostly focuses on the development of photocatalytic
superwetting materials for solid–liquid–vapor phase. Development of underwater superoleophobic materials is gaining attention
due to their applications in waste water treatments and separation of oil-in-water emulsions. Further studies are required to
understand the structure-wettability patterns of these groups of
materials. Rational design of multifunctional TiO2 materials by
integrating biological inspired self-cleaning structure with tunable
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
wettability will be a promising strategy to address the current
energy and environmental problems.
Acknowledgements
The authors wish to acknowledge financial support under the U.
S.–Ireland R&D Partnership programme from the Science Foundation Ireland (SFI-grant number 10/US/I1822 (T)) and U. S. National
Science Foundation-CBET (Award 1033317). D.D. Dionysiou also
acknowledges support from the University of Cincinnati through
a UNESCO co-Chair Professor position on “Water Access and Sustainability”.
References
[1] K. Liu, M. Cao, A. Fujishima, L. Jiang, Chem. Rev. 114 (2014) 10044–10094.
[2] K. Qi, W.A. Daoud, J.H. Xin, C.L. Mak, W. Tang, W.P. Cheung, J. Mater. Chem.
16 (2006) 4567–4574.
[3] W.S. Tung, W.A. Daoud, J. Mater. Chem. 21 (2011) 7858–7869.
[4] H. Yaghoubi, N. Taghavinia, E.K. Alamdari, Surf. Coat. Technol. 204 (2010)
1562–1568.
[5] Y. Takata, S. Hidaka, J.M. Cao, T. Nakamura, H. Yamamoto, M. Masuda, T. Ito,
Energy 30 (2005) 209–220.
[6] T. Watanabe, A. Nakajima, R. Wang, M. Minabe, S. Koizumi, A. Fujishima, K.
Hashimoto, Thin Solid Films 351 (1999) 260–263.
[7] R. Wang, K. Hashimoto, A. Fujishima, M. Chikuni, E. Kojima, A. Kitamura, M.
Shimohigoshi, T. Watanabe, Nature 388 (1997) 431–432.
[8] I.P. Parkin, R.G. Palgrave, J. Mater. Chem. 15 (2005) 1689–1695.
[9] A. Mills, A. Lepre, N. Elliott, S. Bhopal, I.P. Parkin, S.A. O’Neill, J. Photochem.
Photobiol. A 160 (2003) 213–224.
[10] T.-H. Xie, J. Lin, J. Phys. Chem. C 111 (2007) 9968–9974.
[11] F. Bondioli, R. Taurino, A.M. Ferrari, J. Colloid Interface Sci. 334 (2009)
195–201.
[12] R.W. Andrews, A. Pollard, J.M. Pearce, Sol. Energy Mater. Sol. Cells 113
(2013) 71–78.
[13] R.M. Fillion, A.R. Riahi, A. Edrisy, Renew. Sustain. Energy Rev. 32 (2014)
797–809.
[14] L. Oberli, D. Caruso, C. Hall, M. Fabretto, P.J. Murphy, D. Evans, Adv. Colloid
Interface Sci. 210 (2014) 47–57.
[15] W. Li, A. Amirfazli, Adv. Colloid Interface Sci. 132 (2007) 51–68.
[16] W. Barthlott, C. Neinhuis, Planta 202 (1997) 1–8.
[17] L. Feng, S. Li, Y. Li, H. Li, L. Zhang, J. Zhai, Y. Song, B. Liu, L. Jiang, D. Zhu, Adv.
Mater. 14 (2002) 1857–1860.
[18] G.D. Bixler, B. Bhushan, Soft Matter 8 (2012) 11271–11284.
[19] M.E. Hay, J. Exp. Mar. Biol. Ecol. 200 (1996) 103–134.
[20] Y. Zhang, H. Wu, X. Yu, F. Chen, J. Wu, J. Bionic Eng. 9 (2012) 84–90.
[21] L. Zhang, R. Dillert, D. Bahnemann, M. Vormoor, Energy Environ. Sci. 5
(2012) 7491–7507.
[22] S. Nishimoto, B. Bhushan, RSC Adv. 3 (2013) 671–690.
[23] G.D. Bixler, B. Bhushan, Crit. Rev. Solid State Mater. Sci. 40 (2014) 1–37.
[24] N. Zhao, Z. Wang, C. Cai, H. Shen, F. Liang, D. Wang, C. Wang, T. Zhu, J. Guo, Y.
Wang, X. Liu, C. Duan, H. Wang, Y. Mao, X. Jia, H. Dong, X. Zhang, J. Xu, Adv.
Mater. 26 (2014) 6994–7017.
[25] G.D. Bixler, A. Theiss, B. Bhushan, S.C. Lee, J. Colloid Interface Sci. 419 (2014)
114–133.
[26] K. Liu, Y. Tian, L. Jiang, Prog. Mater. Sci. 58 (2013) 503–564.
[27] K. Liu, X. Yao, L. Jiang, Chem. Soc. Rev. 39 (2010) 3240–3255.
[28] A. Fujishima, X. Zhang, D.A. Tryk, Surf. Sci. Rep. 63 (2008) 515–582.
[29] K. Nakata, A. Fujishima, J. Photochem. Photobiol. C 13 (2012)
169–189.
[30] P. Ragesh, V. Anand Ganesh, S.V. Nair, A.S. Nair, J. Mater. Chem. A 2 (2014)
14773–14797.
[31] F.Ç. Cebeci, Z. Wu, L. Zhai, R.E. Cohen, M.F. Rubner, Langmuir 22 (2006)
2856–2862.
[32] E. Martines, K. Seunarine, H. Morgan, N. Gadegaard, C.D.W. Wilkinson, M.O.
Riehle, Nano Lett. 5 (2005) 2097–2103.
[33] C. Fang, C. Hidrovo, F.-m. Wang, J. Eaton, K. Goodson, Int. J. Multiphase Flow
34 (2008) 690–705.
[34] L. Gao, T.J. McCarthy, Langmuir 22 (2006) 6234–6237.
[35] R.N. Wenzel, Ind. Eng. Chem. 28 (1936) 988–994.
[36] A.B.D. Cassie, S. Baxter, Trans. Faraday Soc. 40 (1944) 546–551.
[37] M. Miwa, A. Nakajima, A. Fujishima, K. Hashimoto, T. Watanabe, Langmuir
16 (2000) 5754–5760.
[38] A. Borras, A.R. González-Elipe, Langmuir 26 (2010) 15875–15882.
[39] E. Ueda, P.A. Levkin, Adv. Mater. 25 (2013) 1234–1247.
[40] D. Tian, Y. Song, L. Jiang, Chem. Soc. Rev. 42 (2013) 5184–5209.
[41] W. Song, J.F. Mano, Soft Matter 9 (2013) 2985–2999.
[42] X.-T. Zhang, O. Sato, A. Fujishima, Langmuir 20 (2004) 6065–6067.
[43] J.S. Li, E. Ueda, A. Nallapaneni, L.X. Li, P.A. Levkin, Langmuir 28 (2012)
8286–8291.
425
[44] K. Tadanaga, J. Morinaga, A. Matsuda, T. Minami, Chem. Mater. 12 (2000)
590–592.
[45] X. Zhang, M. Jin, Z. Liu, S. Nishimoto, H. Saito, T. Murakami, A. Fujishima,
Langmuir 22 (2006) 9477–9479.
[46] Y. Lai, C. Lin, H. Wang, J. Huang, H. Zhuang, L. Sun, Electrochem. Commun. 10
(2008) 387–391.
[47] Q. Liang, Y. Chen, Y. Fan, Y. Hu, Y. Wu, Z. Zhao, Q. Meng, Appl. Surf. Sci. 258
(2012) 2266–2269.
[48] K. Nakata, S. Nishimoto, A. Kubo, D. Tryk, T. Ochiai, T. Murakami, A.
Fujishima, Chem. – Asian J. 4 (2009) 984–988.
[49] Y. Lai, L. Lin, F. Pan, J. Huang, R. Song, Y. Huang, C. Lin, H. Fuchs, L. Chi, Small
9 (2013) 2945–2953.
[50] M. Pelaez, N.T. Nolan, S.C. Pillai, M.K. Seery, P. Falaras, A.G. Kontos, P.S.M.
Dunlop, J.W.J. Hamilton, J.A. Byrne, K. O’Shea, M.H. Entezari, D.D. Dionysiou,
Appl. Catal. B 125 (2012) 331–349.
[51] M.D. Hernandez-Alonso, F. Fresno, S. Suarez, J.M. Coronado, Energy Environ.
Sci. 2 (2009) 1231–1257.
[52] Y. Zheng, J. Liu, J. Liang, M. Jaroniec, S.Z. Qiao, Energy Environ. Sci. 5 (2012)
6717–6731.
[53] H. Kisch, Angew. Chem. Int. Ed. 52 (2013) 812–847.
[54] Y. Inoue, Energy Environ. Sci. 2 (2009) 364–386.
[55] D.A. Keane, K.G. McGuigan, P.F. Ibanez, M.I. Polo-Lopez, J.A. Byrne, P.S.M.
Dunlop, K. O’Shea, D.D. Dionysiou, S.C. Pillai, Catal. Sci. Technol. 4 (2014)
1211–1226.
[56] M.B. Fisher, D.A. Keane, P. Fernández-Ibáñez, J. Colreavy, S.J. Hinder, K.G.
McGuigan, S.C. Pillai, Appl. Catal. B 130–131 (2013) 8–13.
[57] S. Banerjee, S.C. Pillai, P. Falaras, K.E. O’shea, J.A. Byrne, D.D. Dionysiou, J.
Phys. Chem. Lett. 5 (2014) 2543–2554.
[58] Y. Qu, X. Duan, Chem. Soc. Rev. 42 (2013) 2568–2580.
[59] J.B. Joo, Q. Zhang, M. Dahl, I. Lee, J. Goebl, F. Zaera, Y. Yin, Energy Environ. Sci.
5 (2012) 6321–6327.
[60] G. Liu, L.-C. Yin, J. Wang, P. Niu, C. Zhen, Y. Xie, H.-M. Cheng, Energy Environ.
Sci. 5 (2012) 9603–9610.
[61] Z. Zhao, H. Tan, H. Zhao, D. Li, M. Zheng, P. Du, G. Zhang, D. Qu, Z. Sun, H. Fan,
Chem. Commun. 49 (2013) 8958–8960.
[62] T. Shibata, N. Sakai, K. Fukuda, Y. Ebina, T. Sasaki, Phys. Chem. Chem. Phys. 9
(2007) 2413–2420.
[63] V.A. Ganesh, A.S. Nair, H.K. Raut, T.M. Walsh, S. Ramakrishna, RSC Adv. 2
(2012) 2067–2072.
[64] N. Sakai, A. Fujishima, T. Watanabe, K. Hashimoto, J. Phys. Chem. B 107
(2003) 1028–1035.
[65] N. Sakai, A. Fujishima, T. Watanabe, K. Hashimoto, J. Phys. Chem. B 105
(2001) 3023–3026.
[66] T. Zubkov, D. Stahl, T.L. Thompson, D. Panayotov, O. Diwald, J.T. Yates, J.
Phys. Chem. B 109 (2005) 15454–15462.
[67] R. Wang, K. Hashimoto, A. Fujishima, M. Chikuni, E. Kojima, A. Kitamura, M.
Shimohigoshi, T. Watanabe, Adv. Mater. 10 (1998) 135–138.
[68] A. Nakajima, S.-i. Koizumi, T. Watanabe, K. Hashimoto, J. Photochem.
Photobiol. A 146 (2001) 129–132.
[69] R. Wang, N. Sakai, A. Fujishima, T. Watanabe, K. Hashimoto, J. Phys. Chem. B
103 (1999) 2188–2194.
[70] A. Nakajima, S.-i. Koizumi, T. Watanabe, K. Hashimoto, Langmuir 16 (2000)
7048–7050.
[71] T. Shibata, H. Irie, K. Hashimoto, Chem. Commun. 25 (2009) 3735–3737.
[72] N. Sakai, R. Wang, A. Fujishima, T. Watanabe, K. Hashimoto, Langmuir 14
(1998) 5918–5920.
[73] M. Kamei, T. Mitsuhashi, Surf. Sci. 463 (2000) L609–L612.
[74] M. Takeuchi, K. Sakamoto, G. Martra, S. Coluccia, M. Anpo, J. Phys. Chem. B
109 (2005) 15422–15428.
[75] X. Yan, R. Abe, T. Ohno, M. Toyofuku, B. Ohtani, Thin Solid Films 516 (2008)
5872–5876.
[76] K. Guan, Surf. Coat. Technol. 191 (2005) 155–160.
[77] M. Miyauchi, A. Nakajima, T. Watanabe, K. Hashimoto, Chem. Mater. 14
(2002) 2812–2816.
[78] A.V. Emeline, A.V. Rudakova, M. Sakai, T. Murakami, A. Fujishima, J. Phys.
Chem. C 117 (2013) 12086–12092.
[79] H.Y. Lee, Y.H. Park, K.H. Ko, Langmuir 16 (2000) 7289–7293.
[80] J.-J. Wang, D.-S. Wang, J. Wang, W.-L. Zhao, C.-W. Wang, Surf. Coat. Technol.
205 (2011) 3596–3599.
[81] J. Yu, X. Zhao, Q. Zhao, G. Wang, Mater. Chem. Phys. 68 (2001) 253–259.
[82] A. Murakami, T. Yamaguchi, S.-i. Hirano, K. Kikuta, Thin Solid Films 516
(2008) 3888–3892.
[83] J.L. Gole, J.D. Stout, C. Burda, Y. Lou, X. Chen, J. Phys. Chem. B 108 (2003)
1230–1240.
[84] M. Pelaez, B. Baruwati, R.S. Varma, R. Luque, D.D. Dionysiou, Chem.
Commun. 49 (2013) 10118–10120.
[85] N.T. Nolan, D.W. Synnott, M.K. Seery, S.J. Hinder, A. Van Wassenhoven, S.C.
Pillai, J. Hazard. Mater. 211 (2012) 88–94.
[86] X. Li, P. Liu, Y. Mao, M. Xing, J. Zhang, Appl. Catal. B 164 (2015) 352–359.
[87] S.U.M. Khan, M. Al-Shahry, W.B. Ingler, Science 297 (2002) 2243–2245.
[88] S. Sakthivel, H. Kisch, Angew. Chem. Int. Ed. 42 (2003) 4908–4911.
[89] S.K. Mohapatra, M. Misra, V.K. Mahajan, K.S. Raja, J. Phys. Chem. C 111
(2007) 8677–8685.
[90] H. Irie, Y. Watanabe, K. Hashimoto, Chem. Lett. 32 (2003) 772–773.
[91] Y. Huang, W. Ho, S. Lee, L. Zhang, G. Li, J.C. Yu, Langmuir 24 (2008)
3510–3516.
426
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
[92] Y. Zhang, Z. Zhao, J. Chen, L. Cheng, J. Chang, W. Sheng, C. Hu, S. Cao, Appl.
Catal. B 166 (2015) 644.
[93] C. Lettmann, K. Hildenbrand, H. Kisch, W. Macyk, W.F. Maier, Appl. Catal. B
32 (2001) 215–227.
[94] T. Umebayashi, T. Yamaki, S. Tanaka, K. Asai, Chem. Lett. 32 (2003) 330–331.
[95] T. Ohno, M. Akiyoshi, T. Umebayashi, K. Asai, T. Mitsui, M. Matsumura, Appl.
Catal. A 265 (2004) 115–121.
[96] R. Asahi, T. Morikawa, T. Ohwaki, K. Aoki, Y. Taga, Science 293 (2001)
269–271.
[97] N. Serpone, J. Phys. Chem. B 110 (2006) 24287–24293.
[98] C. Di Valentin, E. Finazzi, G. Pacchioni, A. Selloni, S. Livraghi, M.C. Paganini, E.
Giamello, Chem. Phys. 339 (2007) 44–56.
[99] C. Di Valentin, G. Pacchioni, Catal. Today 206 (2013) 12–18.
[100] C. Di Valentin, G. Pacchioni, A. Selloni, S. Livraghi, E. Giamello, J. Phys. Chem.
B 109 (2005) 11414–11419.
[101] F. Napoli, M. Chiesa, S. Livraghi, E. Giamello, S. Agnoli, G. Granozzi, G.
Pacchioni, C. Di Valentin, Chem. Phys. Lett. 477 (2009) 135–138.
[102] H. Irie, S. Washizuka, N. Yoshino, K. Hashimoto, Chem. Commun. 11 (2003)
1298–1299.
[103] J. Premkumar, Chem. Mater. 16 (2004) 3980–3981.
[104] C.W. Dunnill, Z. Ansari, A. Kafizas, S. Perni, D.J. Morgan, M. Wilson, I.P.
Parkin, J. Mater. Chem. 21 (2011) 11854–11861.
[105] H. Irie, S. Washizuka, K. Hashimoto, Thin Solid Films 510 (2006) 21–25.
[106] J. Tang, H. Quan, J. Ye, Chem. Mater. 19 (2006) 116–122.
[107] A.M. Czoska, S. Livraghi, M. Chiesa, E. Giamello, S. Agnoli, G. Granozzi, E.
Finazzi, C.D. Valentin, G. Pacchioni, J. Phys. Chem. C 112 (2008) 8951–8956.
[108] J.-H. Xu, J. Li, W.-L. Dai, Y. Cao, H. Li, K. Fan, Appl. Catal. B 79 (2008) 72–80.
[109] G. Liu, C. Han, M. Pelaez, D. Zhu, S. Liao, V. Likodimos, A.G. Kontos, P. Falaras,
D.D. Dionysiou, J. Mol. Catal. A: Chem. 372 (2013) 58–65.
[110] P. Periyat, D.E. McCormack, S.J. Hinder, S.C. Pillai, J. Phys. Chem. C 113 (2009)
3246–3253.
[111] A.V. Katsanaki, A.G. Kontos, T. Maggos, M. Pelaez, V. Likodimos, E.A.
Pavlatou, D.D. Dionysiou, P. Falaras, Appl. Catal. B 140 (2013) 619–625.
[112] M. Pelaez, P. Falaras, A.G. Kontos, A.A. de la Cruz, K. O’Shea, P.S.M. Dunlop,
J.A. Byrne, D.D. Dionysiou, Appl. Catal. B 121 (2012) 30–39.
[113] J.W.J. Hamilton, J.A. Byrne, P.S.M. Dunlop, D.D. Dionysiou, M. Pelaez, K.
O’Shea, D. Synnott, S.C. Pillai, J. Phys. Chem. C 118 (2014) 12206–12215.
[114] Y.W. Sakai, K. Obata, K. Hashimoto, H. Irie, Vacuum 83 (2008) 683–687.
[115] A.G. Kontos, M. Pelaez, V. Likodimos, N. Vaenas, D.D. Dionysiou, P. Falaras,
Photochem. Photobiol. Sci. 10 (2011) 350–354.
[116] Q.-C. Xu, D.V. Wellia, M.A. Sk, K.H. Lim, J.S.C. Loo, D.W. Liao, R. Amal, T.T.Y.
Tan, J. Photochem. Photobiol. A 210 (2010) 181–187.
[117] Q. Li, J.K. Shang, Environ. Sci. Technol. 44 (2010) 3493–3499.
[118] A. Di Paola, E. Garcıı́a-López, S. Ikeda, G. Marcı`, B. Ohtani, L. Palmisano, Catal.
Today 75 (2002) 87–93.
[119] K.-W. Weng, Y.-P. Huang, Surf. Coat. Technol. 231 (2013) 201–204.
[120] M. Farbod, S. Rezaian, Thin Solid Films 520 (2012) 1954–1958.
[121] A. Eshaghi, A. Eshaghi, Mater. Res. Bull. 46 (2011) 2342–2345.
[122] S. Kitano, N. Murakami, T. Ohno, Y. Mitani, Y. Nosaka, H. Asakura, K.
Teramura, T. Tanaka, H. Tada, K. Hashimoto, H. Kominami, J. Phys. Chem. C
117 (2013) 11008–11016.
[123] J. Xu, Y. Ao, D. Fu, C. Yuan, J. Colloid Interface Sci. 328 (2008) 447–451.
[124] L.G. Devi, S.G. Kumar, Appl. Surf. Sci. 261 (2012) 137–146.
[125] J. Reszczynska, T. Grzyb, J.W. Sobczak, W. Lisowski, M. Gazda, B. Ohtani, A.
Zaleska, Appl. Catal. B 163 (2015) 40–49.
[126] M.K. Seery, R. George, P. Floris, S.C. Pillai, J. Photochem. Photobiol. A 189
(2007) 258–263.
[127] I.M. Arabatzis, T. Stergiopoulos, M.C. Bernard, D. Labou, S.G. Neophytides, P.
Falaras, Appl. Catal. B 42 (2003) 187–201.
[128] N.T. Nolan, M.K. Seery, S.J. Hinder, L.F. Healy, S.C. Pillai, J. Phys. Chem. C 114
(2010) 13026–13034.
[129] S. Linic, P. Christopher, D.B. Ingram, Nat. Mater. 10 (2011) 911–921.
[130] K. Awazu, M. Fujimaki, C. Rockstuhl, J. Tominaga, H. Murakami, Y. Ohki, N.
Yoshida, T. Watanabe, J. Am. Chem. Soc. 130 (2008) 1676–1680.
[131] X. Zhang, H. Yang, A. Tang, J. Phys. Chem. B 112 (2008) 16271–16279.
[132] S. Yang, L.E. Halliburton, A. Manivannan, P.H. Bunton, D.B. Baker, M. Klemm,
S. Horn, A. Fujishima, Appl. Phys. Lett. 94 (2009) 162114.
[133] M.R. Bayati, R. Molaei, F. Golestani-Fard, Colloids Surf. A 373 (2011) 51–60.
[134] L. Zang, W. Macyk, C. Lange, W.F. Maier, C. Antonius, D. Meissner, H. Kisch,
Chem. – Eur. J. 6 (2000) 379–384.
[135] L. Jing, B. Xin, F. Yuan, L. Xue, B. Wang, H. Fu, J. Phys. Chem. B 110 (2006)
17860–17865.
[136] Y. Qu, S. Song, L. Jing, Y. Luan, H. Fu, Thin Solid Films 518 (2010) 3177–3181.
[137] M. Yang, C. Hume, S. Lee, Y.-H. Son, J.-K. Lee, J. Phys. Chem. C 114 (2010)
15292–15297.
[138] S.S. Thind, G. Wu, A. Chen, Appl. Catal. B 111–112 (2012) 38–45.
[139] J. Liu, R. Han, Y. Zhao, H. Wang, W. Lu, T. Yu, Y. Zhang, J. Phys. Chem. C 115
(2011) 4507–4515.
[140] Y.-F. Li, D. Xu, J.I. Oh, W. Shen, X. Li, Y. Yu, ACS Catal. 2 (2012) 391–398.
[141] X. Wu, S. Yin, Q. Dong, C. Guo, T. Kimura, J.-i. Matsushita, T. Sato, J. Phys.
Chem. C 117 (2013) 8345–8352.
[142] Y. Niu, M. Xing, J. Zhang, B. Tian, Catal. Today 201 (2013) 159–166.
[143] E. Wang, T. He, L. Zhao, Y. Chen, Y. Cao, J. Mater. Chem. 21 (2011) 144–150.
[144] H. Liu, Y. Wu, J. Zhang, ACS Appl. Mater. Interfaces 3 (2011) 1757–1764.
[145] N. Feng, Q. Wang, A. Zheng, Z. Zhang, J. Fan, S.-B. Liu, J.-P. Amoureux, F. Deng,
J. Am. Chem. Soc. 135 (2013) 1607–1616.
[146] D.S. Tsoukleris, A.I. Kontos, P. Aloupogiannis, P. Falaras, Catal. Today 124
(2007) 110–117.
[147] P. Falaras, Sol. Energy Mater. Sol. Cells 53 (1998) 163–175.
[148] J. Zhao, C. Chen, W. Ma, Top. Catal. 35 (2005) 269–278.
[149] M. Zhang, C. Chen, W. Ma, J. Zhao, Angew. Chem. Int. Ed. 47 (2008)
9730–9733.
[150] X. Li, L. Liu, S.-Z. Kang, J. Mu, G. Li, Appl. Surf. Sci. 257 (2011) 5950–5956.
[151] S. Afzal, W.A. Daoud, S.J. Langford, ACS Appl. Mater. Interfaces 5 (2013)
4753–4759.
[152] S.-H. Wu, J.-L. Wu, S.-Y. Jia, Q.-W. Chang, H.-T. Ren, Y. Liu, Appl. Surf. Sci. 287
(2013) 389–396.
[153] D. Kuang, S. Ito, B. Wenger, C. Klein, J.-E. Moser, R. Humphry-Baker, S.M.
Zakeeruddin, M. Grätzel, J. Am. Chem. Soc. 128 (2006) 4146–4154.
[154] A. Hagfeldt, M. Grätzel, Acc. Chem. Res. 33 (2000) 269–277.
[155] R. Argazzi, G. Larramona, C. Contado, C.A. Bignozzi, J. Photochem. Photobiol.
A 164 (2004) 15–21.
[156] A. Islam, H. Sugihara, K. Hara, L.P. Singh, R. Katoh, M. Yanagida, Y. Takahashi,
S. Murata, H. Arakawa, New J. Chem. 24 (2000) 343–345.
[157] B. Gholamkhass, H. Mametsuka, K. Koike, T. Tanabe, M. Furue, O. Ishitani,
Inorg. Chem. 44 (2005) 2326–2336.
[158] S. Afzal, W.A. Daoud, S.J. Langford, Appl. Surf. Sci. 275 (2013) 36–42.
[159] B.-K. An, W. Hu, P.L. Burn, P. Meredith, J. Phys. Chem. C 114 (2010)
17964–17974.
[160] F.-X. Xiao, ACS Appl. Mater. Interfaces 4 (2012) 7055–7063.
[161] B. Liu, A. Khare, E.S. Aydil, ACS Appl. Mater. Interfaces 3 (2011) 4444–4450.
[162] V. Etacheri, G. Michlits, M.K. Seery, S.J. Hinder, S.C. Pillai, ACS Appl. Mater.
Interfaces 5 (2013) 1663–1672.
[163] V. Etacheri, M.K. Seery, S.J. Hinder, S.C. Pillai, Chem. Mater. 22 (2010)
3843–3853.
[164] V. Etacheri, M.K. Seery, S.J. Hinder, S.C. Pillai, Inorg. Chem. 51 (2012)
7164–7173.
[165] M. Miyauchi, A. Nakajima, T. Watanabe, K. Hashimoto, Chem. Mater. 14
(2002) 4714–4720.
[166] M. Miyauchi, A. Nakajima, K. Hashimoto, T. Watanabe, Adv. Mater. 12 (2000)
1923–1927.
[167] A. Srinivasan, M. Miyauchi, J. Phys. Chem. C 116 (2012) 15421–15426.
[168] A.O.T. Patrocinio, L.F. Paula, R.M. Paniago, J. Freitag, D.W. Bahnemann, ACS
Appl. Mater. Interfaces 6 (2014) 16859–16866.
[169] G. Tian, Y. Chen, R. Zhai, J. Zhou, W. Zhou, R. Wang, K. Pan, C. Tian, H. Fu, J.
Mater. Chem. A 1 (2013) 6961–6968.
[170] T.H. Jun, K.-S. Lee, H.S. Song, Thin Solid Films 520 (2012) 2609–2612.
[171] R. Wang, H. Tan, Z. Zhao, G. Zhang, L. Song, W. Dong, Z. Sun, J. Mat. Chem. A 2
(2014) 7313–7318.
[172] R. Fateh, R. Dillert, D. Bahnemann, ACS Appl. Mater. Interfaces 6 (2014)
2270–2278.
[173] Y. Abdi, M. Khalilian, E. Arzi, J. Phys. D: Appl. Phys. 44 (2011) 255405.
[174] D. Wang, D. Choi, J. Li, Z. Yang, Z. Nie, R. Kou, D. Hu, C. Wang, L.V. Saraf, J.
Zhang, I.A. Aksay, J. Liu, ACS Nano 3 (2009) 907–914.
[175] A. Cao, Z. Liu, S. Chu, M. Wu, Z. Ye, Z. Cai, Y. Chang, S. Wang, Q. Gong, Y. Liu,
Adv. Mater. 22 (2010) 103–106.
[176] Y.H. Ng, A. Iwase, A. Kudo, R. Amal, J. Phys. Chem. Lett. 1 (2010) 2607–2612.
[177] S. Anandan, T. Narasinga Rao, M. Sathish, D. Rangappa, I. Honma, M.
Miyauchi, ACS Appl. Mater. Interfaces 5 (2012) 207–212.
[178] L. Karimi, M.E. Yazdanshenas, R. Khajavi, A. Rashidi, M. Mirjalili, Cellulose 21
(2014) 3813–3827.
[179] J. Zhu, Y. Cao, J. He, J. Colloid Interface Sci. 420 (2014) 119–126.
[180] P. Nostell, A. Roos, B. Karlsson, Thin Solid Films 351 (1999) 170–175.
[181] Y.-J. Lee, D.S. Ruby, D.W. Peters, B.B. McKenzie, J.W.P. Hsu, Nano Lett. 8
(2008) 1501–1505.
[182] B.S. Richards, Sol. Energy Mater. Sol. Cells 79 (2003) 369–390.
[183] Z. Liu, X. Zhang, T. Murakami, A. Fujishima, Sol. Energy Mater. Sol. Cells 92
(2008) 1434–1438.
[184] M. Faustini, L. Nicole, C. Boissière, P. Innocenzi, C. Sanchez, D. Grosso, Chem.
Mater. 22 (2010) 4406–4413.
[185] X.-T. Zhang, O. Sato, M. Taguchi, Y. Einaga, T. Murakami, A. Fujishima, Chem.
Mater. 17 (2005) 696–700.
[186] L. Yao, J. He, Prog. Mater. Sci. 61 (2014) 94–143.
[187] J. Cai, J. Ye, S. Chen, X. Zhao, D. Zhang, S. Chen, Y. Ma, S. Jin, L. Qi, Energy
Environ. Sci. 5 (2012) 7575–7581.
[188] M. Houmard, G. Berthomé, J.C. Joud, M. Langlet, Surf. Sci. 605 (2011)
456–462.
[189] M. Houmard, D. Riassetto, F. Roussel, A. Bourgeois, G. Berthomé, J.C. Joud, M.
Langlet, Surf. Sci. 602 (2008) 3364–3374.
[190] Y.Y. Liu, L.Q. Qian, C. Guo, X. Jia, J.W. Wang, W.H. Tang, J. Alloys Compd. 479
(2009) 532–535.
[191] Y.J. Xu, J.X. Liao, Q.W. Cai, X.X. Yang, Sol. Energy Mater. Sol. Cells 113 (2013)
7–12.
[192] A. Tricoli, M. Righettoni, S.E. Pratsinis, Langmuir 25 (2009) 12578–12584.
[193] K. Guan, B. Lu, Y. Yin, Surf. Coat. Technol. 173 (2003) 219–223.
[194] X. Zhang, F. Zhang, K.-Y. Chan, Appl. Catal. A 284 (2005) 193–198.
[195] C. Kapridaki, L. Pinho, M.J. Mosquera, P. Maravelaki-Kalaitzaki, Appl. Catal. B
156 (2014) 416–427.
[196] S.-Y. Lien, A. Nautiyal, J.-H. Jhu, J.-K. Hsu, S.J. Lee, Asian J. Chem. 25 (2013)
6071–6074.
[197] T. Huang, W. Huang, C. Zhou, Y. Situ, H. Huang, Surf. Coat. Technol. 213
(2012) 126–132.
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
[198] B. Erdural, U. Bolukbasi, G. Karakas, J. Photochem. Photobiol. A 283 (2014)
29–37.
[199] A. Eshaghi, A. Eshaghi, Appl. Surf. Sci. 258 (2012) 2464–2467.
[200] M. Mokhtarimehr, M. Pakshir, A. Eshaghi, M.H. Shariat, Thin Solid Films 532
(2013) 123–126.
[201] J. Wang, C. Lu, J. Xiong, Appl. Surf. Sci. 298 (2014) 19–25.
[202] E. Pakdel, W.A. Daoud, X. Wang, Appl. Surf. Sci. 275 (2013) 397–402.
[203] E. Pakdel, W.A. Daoud, J. Colloid Interface Sci. 401 (2013) 1–7.
[204] R. Wang, X. Wang, J.H. Xin, ACS Appl. Mater. Interfaces 2 (2009) 82–85.
[205] X. Li, J. He, ACS Appl. Mater. Interfaces 5 (2013) 5282–5290.
[206] K. Nakata, M. Sakai, T. Ochiai, T. Murakami, K. Takagi, A. Fujishima, Langmuir
27 (2011) 3275–3278.
[207] K. Nakata, C. Terashima, A. Fujishima, Chem. Lett. 43 (2014) 1511–1513.
[208] <https://http://www.asme.org/engineering-topics/articles/energy/
self-cleaning-solar-panels-maximize-efficiency>.
[209] J. Zhu, C.-M. Hsu, Z. Yu, S. Fan, Y. Cui, Nano Lett. 10 (2010) 1979–1984.
[210] S. Guldin, P. Kohn, M. Stefik, J. Song, G. Divitini, F. Ecarla, C. Ducati, U.
Wiesner, U. Steiner, Nano Lett. 13 (2013) 5329–5335.
[211] Q. Mu, Y. Li, H. Wang, Q. Zhang, J. Colloid Interface Sci. 365 (2012) 308–313.
[212] Q.-c. Xu, D.V. Wellia, M.A. Sk, K.H. Lim, J.S.C. Loo, D.W. Liao, R. Amal, T.T.Y.
Tan, J. Photochem. Photobiol. A 210 (2010) 181–187.
[213] H.M. Yadav, S.V. Otari, R.A. Bohara, S.S. Mali, S.H. Pawar, S.D. Delekar, J.
Photochem. Photobiol. A 294 (2014) 130–136.
[214] G. Fu, P.S. Vary, C.-T. Lin, J. Phys. Chem. B 109 (2005) 8889–8898.
[215] Y. Kikuchi, K. Sunada, T. Iyoda, K. Hashimoto, A. Fujishima, J. Photochem.
Photobiol. A 106 (1997) 51–56.
[216] L. Sun, Y. Qin, Q. Cao, B. Hu, Z. Huang, L. Ye, X. Tang, Chem. Commun. 47
(2011) 12628–12630.
[217] X. Qiu, M. Miyauchi, K. Sunada, M. Minoshima, M. Liu, Y. Lu, D. Li, Y.
Shimodaira, Y. Hosogi, Y. Kuroda, K. Hashimoto, ACS Nano 6 (2011)
1609–1618.
[218] D. Mitoraj, A. Janczyk, M. Strus, H. Kisch, G. Stochel, P.B. Heczko, W. Macyk,
Photochem. Photobiol. Sci. 6 (2007) 642–648.
[219] H. Li, Q. Cui, B. Feng, J. Wang, X. Lu, J. Weng, Appl. Surf. Sci. 284 (2013)
179–183.
[220] X. Chen, K. Cai, J. Fang, M. Lai, J. Li, Y. Hou, Z. Luo, Y. Hu, L. Tang, Surf. Coat.
Technol. 216 (2013) 158–165.
[221] J. Podporska-Carroll, E. Panaitescu, B. Quilty, L. Wang, L. Menon, S.C. Pillai,
Appl. Catal. B 176–177 (2015) 70–75,
http://dx.doi.org/10.1016/j.apcatb.2015.03.029.
[222] C. Hu, J. Guo, J. Qu, X. Hu, Langmuir 23 (2007) 4982–4987.
[223] D. Wu, M. Long, Surf. Coat. Technol. 206 (2011) 1175–1179.
[224] Y. Xie, Y. Jin, Y. Zhou, Y. Wang, Appl. Surf. Sci. 313 (2014) 549–557.
[225] S.C. Xu, Y.X. Zhang, Y.Y. Luo, S. Wang, H.L. Ding, J.M. Xu, G.H. Li, Analyst 138
(2013) 4519–4525.
[226] K. Sunada, Y. Kikuchi, K. Hashimoto, A. Fujishima, Environ. Sci. Technol. 32
(1998) 726–728.
[227] Z.-X. Lu, L. Zhou, Z.-L. Zhang, W.-L. Shi, Z.-X. Xie, H.-Y. Xie, D.-W. Pang, P.
Shen, Langmuir 19 (2003) 8765–8768.
[228] J.A. Rengifo-Herrera, K. Pierzchała, A. Sienkiewicz, L. Forró, J. Kiwi, C.
Pulgarin, Appl. Catal. B 88 (2009) 398–406.
[229] J.A. Rengifo-Herrera, C. Pulgarin, Sol. Energy 84 (2010) 37–43.
[230] M. Macias-Montero, A. Borras, Z. Saghi, P. Romero-Gomez, J.R.
Sanchez-Valencia, J.C. Gonzalez, A. Barranco, P. Midgley, J. Cotrino, A.R.
Gonzalez-Elipe, J. Mater. Chem. 22 (2012) 1341–1346.
[231] T. Watanabe, N. Yoshida, Chem. Rec. 8 (2008) 279–290.
[232] N. Yoshida, M. Takeuchi, T. Okura, H. Monma, M. Wakamura, H. Ohsaki, T.
Watanabe, Thin Solid Films 502 (2006) 108–111.
[233] P. Ragesh, S.V. Nair, A.S. Nair, RSC Adv. 4 (2014) 38498–38504.
[234] C.R. Crick, S. Ismail, J. Pratten, I.P. Parkin, Thin Solid Films 519 (2011)
3722–3727.
[235] S. Wooh, J.H. Koh, S. Lee, H. Yoon, K. Char, Adv. Funct. Mater. 24 (2014)
5550–5556.
[236] C.R. Crick, I.P. Parkin, Chem. Eur. J. 16 (2010) 3568–3588.
[237] A. Nakajima, K. Hashimoto, T. Watanabe, K. Takai, G. Yamauchi, A. Fujishima,
Langmuir 16 (2000) 7044–7047.
[238] M. Wakamura, K. Hashimoto, T. Watanabe, Langmuir 19 (2003) 3428–3431.
[239] T. Kamegawa, Y. Shimizu, H. Yamashita, Adv. Mater. 24 (2012) 3697–3700.
[240] C.R. Crick, J.C. Bear, A. Kafizas, I.P. Parkin, Adv. Mater. 24 (2012) 3505–3508.
[241] X. Zhang, Y. Guo, Z. Zhang, P. Zhang, Appl. Surf. Sci. 284 (2013) 319–323.
[242] Q.F. Xu, Y. Liu, F.-J. Lin, B. Mondal, A.M. Lyons, ACS Appl. Mater. Interfaces 5
(2013) 8915–8924.
[243] I. Kartini, S. Santosa, E. Febriyanti, O. Nugroho, H. Yu, L. Wang, J. Nanopart.
Res. 16 (2014) 1–14.
[244] A. Uyama, S. Yamazoe, S. Shigematsu, M. Morimoto, S. Yokojima, H. Mayama,
Y. Kojima, S. Nakamura, K. Uchida, Langmuir 27 (2011) 6395–6400.
[245] P. Wan, Y. Jiang, Y. Wang, Z. Wang, X. Zhang, Chem. Commun. 44 (2008)
5710–5712.
[246] K. Ichimura, S.-K. Oh, M. Nakagawa, Science 288 (2000) 1624–1626.
[247] T. Onda, S. Shibuichi, N. Satoh, K. Tsujii, Langmuir 12 (1996) 2125–2127.
[248] W. Li, T. Guo, T. Meng, Y. Huang, X. Li, W. Yan, S. Wang, X. Li, Appl. Surf. Sci.
283 (2013) 12–18.
[249] U. Lehmann, S. Hadjidj, V.K. Parashar, C. Vandevyver, A. Rida, M.A.M. Gijs,
Sens. Actuators B 117 (2006) 457–463.
[250] D.A. LaVan, T. McGuire, R. Langer, Nat. Biotechnol. 21 (2003) 1184–1191.
[251] K. Koch, B. Bhushan, W. Barthlott, Prog. Mater. Sci. 54 (2009) 137–178.
427
[252] M. Järn, Q. Xu, M. Lindén, Langmuir 26 (2010) 11330–11336.
[253] B. Yan, J. Tao, C. Pang, Z. Zheng, Z. Shen, C.H.A. Huan, T. Yu, Langmuir 24
(2008) 10569–10571.
[254] A. Mills, C. Hill, P.K.J. Robertson, J. Photochem. Photobiol. A 237 (2012) 7–23.
[255] L. Zhang, Y. Zhong, D. Cha, P. Wang, Sci. Rep. 3 (2013) 1–5.
[256] Y. Sawai, S. Nishimoto, Y. Kameshima, E. Fujii, M. Miyake, Langmuir 29
(2013) 6784–6789.
[257] H. Wang, Z. Guo, Appl. Phys. Lett. 104 (2014) 183703.
[258] S.J. Gao, Z. Shi, W.B. Zhang, F. Zhang, J. Jin, ACS Nano 8 (2014) 6344–6352.
[259] P. Gao, Z. Liu, D.D. Sun, W.J. Ng, J. Mater. Chem. A 2 (2014) 14082–14088.
[260] W. Zhu, X. Feng, L. Feng, L. Jiang, Chem. Commun. 26 (2006) 2753–2755.
[261] R. Andre, F. Natalio, M.N. Tahir, R. Berger, W. Tremel, Nanoscale 5 (2013)
3447–3456.
[262] J. Pan, X. Song, J. Zhang, H. Shen, Q. Xiong, J. Phys. Chem. C 115 (2011)
22225–22231.
[263] R.-D. Sun, A. Nakajima, A. Fujishima, T. Watanabe, K. Hashimoto, J. Phys.
Chem. B 105 (2001) 1984–1990.
[264] Y. Zang, J. Yin, X. He, C. Yue, Z. Wu, J. Li, J. Kang, J. Mater. Chem. A 2 (2014)
7747–7753.
[265] Z. Guo, X. Chen, J. Li, J.-H. Liu, X.-J. Huang, Langmuir 27 (2011) 6193–6200.
[266] S. Balachandran, N. Prakash, K. Thirumalai, M. Muruganandham, M.
Sillanpää, M. Swaminathan, Ind. Eng. Chem. Res. 53 (2014) 8346–8356.
[267] T. Kako, J. Ye, Langmuir 23 (2006) 1924–1927.
[268] T. Shibata, G. Takanashi, T. Nakamura, K. Fukuda, Y. Ebina, T. Sasaki, Energy
Environ. Sci. 4 (2011) 535–542.
[269] in: ISO 27448: 2009 Fine ceramics (advanced ceramics, advanced technical
ceramics) – Test method for self-cleaning performance of semiconducting
photocatalytic materials – Measurement of water contact angle.
[270] in: ISO 10678: 2010 Fine ceramics (advanced ceramics, advanced technical
ceramics) – Determination of photocatalytic activity of surfaces in an
aqueous medium by degradation of methylene blue.
[271] A. Houas, H. Lachheb, M. Ksibi, E. Elaloui, C. Guillard, J.-M. Herrmann, Appl.
Catal. B 31 (2001) 145–157.
[272] J. Krýsa, P. Novotná, Š. Kment, A. Mills, J. Photochem. Photobiol. A 222 (2011)
81–86.
[273] in: ISO 27447: 2009, ‘Fine ceramics, advanced technical ceramics – Test
method for antibacterial activity of semiconducting photocatalytic
materials .
[274] J. Krýsa, E. Musilová, J. Zita, J. Hazard. Mater. 195 (2011) 100–106.
[275] A. Mills, J. Hepburn, D. Hazafy, C. O’Rourke, J. Krysa, M. Baudys, M. Zlamal, H.
Bartkova, C.E. Hill, K.R. Winn, M.E. Simonsen, E.G. Søgaard, S.C. Pillai, N.S.
Leyland, R. Fagan, F. Neumann, C. Lampe, T. Graumann, J. Photochem.
Photobiol. A 272 (2013) 18–20.
[276] A. Mills, J. Hepburn, D. Hazafy, C. O’Rourke, N. Wells, J. Krysa, M. Baudys, M.
Zlamal, H. Bartkova, C.E. Hill, K.R. Winn, M.E. Simonsen, E.G. Søgaard, S.
Banerjee, R. Fagan, S.C. Pillai, J. Photochem. Photobiol. A 290 (2014) 63–71.
[277] A. Mills, N. Wells, C. O’Rourke, Catal. Today 230 (2014) 245–249.
[278] A. Mills, N. Wells, Chem. Soc. Rev. (2015),
http://dx.doi.org/10.1039/C4CS00279B.
[279] A. Mills, J. Wang, S.-K. Lee, M. Simonsen, Chem. Commun. 21 (2005)
2721–2723.
[280] H.-Y. Chun, S.-S. Park, S.-H. You, G.-H. Kang, W.-T. Bae, K.-W. Kim, J.-E. Park,
A. Ozturk, D.-W. Shin, J. Ceram. Process. Res. 10 (2009) 219–223.
[281] V.S. Smitha, K.A. Manjumol, K.V. Baiju, S. Ghosh, P. Perumal, K.G.K. Warrier, J.
Sol–Gel Sci. Technol. 54 (2010) 203–211.
[282] M. Radeka, S. Markov, E. Lončar, O. Rudić, S. Vučetić, J. Ranogajec, J. Eur.
Ceram. Soc. 34 (2014) 127–136.
[283] S. Ke, X. Cheng, Q. Wang, Y. Wang, Z. Pan, Ceram. Int. 40 (2014) 8891–8895.
[284] K. Midtdal, B.P. Jelle, Sol. Energy Mater. Sol. Cells 109 (2013) 126–141.
[285] <http://www.activglass.com/index.eng.htm>, (accessed 18.03.15).
[286] M. Shimohigoshi, Y. Saeki, Research and applications of photocatalyst tiles,
in: P. Baglioni, L. Casssar (Eds.), International RILEM Symposium on
Photocatalysis, Environment and Construction Materials – TDP 2007, RILEM
Publications SARL, 2007, pp. 291–297.
[287] P. Periyat, S.C. Pillai, D.E. McCormack, J. Colreavy, S.J. Hinder, J. Phys. Chem. C
112 (2008) 7644–7652.
[288] M. Yan, F. Chen, J. Zhang, M. Anpo, J. Phys. Chem. B 109 (2005) 8673–8678.
[289] V. Etacheri, M.K. Seery, S.J. Hinder, S.C. Pillai, Adv. Funct. Mater. 21 (2011)
3744–3752.
[290] Y. Lu, S. Sathasivam, J. Song, C.R. Crick, C.J. Carmalt, I.P. Parkin, Science 347
(2015) 1132–1135.
[291] C. Bai, Science 309 (2005) 61–63.
[292] L. Cassar, MRS Bull. 29 (2004) 328–331.
[293] <http://www.italcementigroup.com/ENG/Research+and+Innovation
/Innovative+Products/TX+Active/>, (accessed 28.02.15).
[294] <http://www.heidelbergcement.com/NR/rdonlyres/28528B72
-3125-4370-B657-616609415500/0/TioCem Broschuere englisch.pdf>,
(accessed 28.02.15).
[295] D. Spasiano, R. Marotta, S. Malato, P. Fernandez-Ibañez, I. Di Somma, Appl.
Catal. B 170–171 (2015) 90–123.
[296] J.O. Carneiro, V. Teixeira, A. Portinha, A. Magalhães, P. Coutinho, C.J. Tavares,
R. Newton, Mater. Sci. Eng. B 138 (2007) 144–150.
[297] K. Murugan, R. Subasri, T.N. Rao, A.S. Gandhi, B.S. Murty, Prog. Org. Coat. 76
(2013) 1756–1760.
[298] P. Zhang, J. Tian, R. Xu, G. Ma, Appl. Surf. Sci. 266 (2013) 141–147.
[299] J. Chen, C.-s. Poon, Build. Environ. 44 (2009) 1899–1906.
428
S. Banerjee et al. / Applied Catalysis B: Environmental 176 (2015) 396–428
[300] P. Amézaga-Madrid, G.V. Nevárez-Moorillón, E. Orrantia-Borunda, M.
Miki-Yoshida, FEMS Microbiol. Lett. 211 (2002) 183–188.
[301] A. Mills, S.-K. Lee, J. Photochem. Photobiol. A 152 (2002) 233–247.
[302] M. Radetić, J. Photochem. Photobiol. C 16 (2013) 62–76.
[303] M. Montazer, E. Pakdel, J. Photochem. Photobiol. C 12 (2011) 293–303.
[304] O.L. Galkina, A. Sycheva, A. Blagodatskiy, G. Kaptay, V.L. Katanaev, G.A.
Seisenbaeva, V.G. Kessler, A.V. Agafonov, Surf. Coat. Technol. 253 (2014)
171–179.
[305] P.A.A.P. Marques, T. Trindade, C.P. Neto, Compos. Sci. Technol. 66 (2006)
1038–1044.
[306] D. Pasqui, R. Barbucci, J. Photochem. Photobiol. A 274 (2014) 1–6.
[307] M.J. Uddin, F. Cesano, F. Bonino, S. Bordiga, G. Spoto, D. Scarano, A. Zecchina,
J. Photochem. Photobiol. A 189 (2007) 286–294.
[308] W. Daoud, J. Xin, J. Sol–Gel Sci. Technol. 29 (2004) 25–29.
[309] W.A. Daoud, J.H. Xin, Y.-H. Zhang, Surf. Sci. 599 (2005) 69–75.
[310] Qi Kaihong, X. Wang, J.H. Xin, Text. Res. J. 81 (2011) 101–110.
[311] L. Karimi, S. Zohoori, A. Amini, New Carbon Mater. 29 (2014) 380–385.
[312] A. Bozzi, T. Yuranova, J. Kiwi, J. Photochem. Photobiol. A 172 (2005)
27–34.
[313] T. Yuranova, R. Mosteo, J. Bandara, D. Laub, J. Kiwi, J. Mol. Catal. A: Chem.
244 (2006) 160–167.
[314] D. Wu, M. Long, ACS Appl. Mater. Interfaces 3 (2011) 4770–4774.
[315] M.J. Uddin, F. Cesano, D. Scarano, F. Bonino, G. Agostini, G. Spoto, S. Bordiga,
A. Zecchina, J. Photochem. Photobiol. A 199 (2008) 64–72.
[316] M. Montazer, A. Behzadnia, M.B. Moghadam, J. Appl. Polym. Sci. 125 (2012)
E356–E363.
[317] D. Mihailović, Z. Šaponjić, V. Vodnik, B. Potkonjak, P. Jovančić, J.M.
Nedeljković, M. Radetić, Polym. Adv. Technol. 22 (2011) 2244–2249.
[318] M. Rehan, A. Hartwig, M. Ott, L. Gätjen, R. Wilken, Surf. Coat. Technol. 219
(2013) 50–58.
[319] S. Afzal, W.A. Daoud, S.J. Langford, J. Mater. Chem. A 2 (2014) 18005–18011.
[320] W.A. Daoud, S.K. Leung, W.S. Tung, J.H. Xin, K. Cheuk, K. Qi, Chem. Mater. 20
(2008) 1242–1244.
[321] W.S. Tung, W.A. Daoud, Acta Biomater. 5 (2009) 50–56.
[322] <http://www.cristalactiv.com/ourproducts/photocat bro voc.pdf>,
(accessed 28.02.15).
[323] <http://www.climasan.com/33671 EN-Pictures-Brochure 6 Pages.pdf>,
(accessed 28.02.15).
[324] J. Auvinen, L. Wirtanen, Atmos. Environ. 42 (2008) 4101–4112.
Dr. Swagata Banerjee completed her BSc (Chemistry
Hons) from Presidency College (University of Calcutta)
and MSc in Biophysics and Molecular Biology from the
University of Calcutta, India. She obtained her PhD (Chemistry) from, Trinity College Dublin, where her project
focused on the synthesis and photophysical studies of
1,8-naphthalimide derivatives and their interactions with
DNA. She joined CREST, Dublin Institute of Technology,
Ireland in 2013, where her research involved developing
titania based functional materials and photocatalysis.
Prof. Dionysios (Dion) D. Dionysiou is currently a Professor of Environmental Engineering and Science, a Herman
Schneider Professor of Engineering and Applied Science,
and UNESCO Co-Chair Professor on “Water Access and
Sustainability”, at the University of Cincinnati. He teaches
courses and performs research in the areas of drinking
water quality and treatment, advanced oxidation technologies and nanotechnologies, and physical–chemical
processes for water quality control. He is currently one
of the editors of Chemical Engineering Journal, Editor of the
Journal of Advanced Oxidation Technologies, Special Issue
Editor of the Journal of Environmental Engineering (ASCE),
and member of the Editorial Boards of several other journals. Dr. Dionysiou is the author or co-author of >200 refereed journal publications,
>90 conference proceedings, >20 book chapter publications, >20 editorials, and >450
presentations. He is currently co-editing three books on water reuse, harmful algal
blooms, and photocatalysis. Dr. Dionysiou’s work received over 8000 citations with
an H factor of 50.
Prof. Suresh C.Pillai obtained his PhD in the area of
Nanotechnology from Trinity College Dublin and then
performed a postdoctoral research at California Institute
of Technology (Caltech), USA. Upon completion of this
appointment he returned to Trinity College Dublin as
a Research Fellow before joining CREST-DIT as a Senior
Research Manager in April 2004. Suresh joined in IT Sligo
as a Senior Lecturer in Environmental Nanotechnology in
October 2013. He is an elected fellow of the UK’s Royal
Microscopical Society (FRMS) and the Institute of Materials, Minerals and Mining (FIMMM). Prof. Suresh was
responsible for acquiring more than D 3 million direct
R&D funding. He has published several scientific articles
in leading peer reviewed journals and has presented in more than forty international conferences. He has delivered over forty international invited talks including
several key-note and plenary talks. He was also the recipient of the ‘Hothouse Commercialization Award 2009’ from the Minister of Science, Technology and Innovation
and also the recipient of the ‘Enterprise Ireland Research Commercialization Award
2009’. He has also been nominated for the ‘One to Watch’ award 2009 for commercializing R&D work (Enterprise Ireland). He has worked as the national delegate and
technical expert for ISO standardization committee and European standardization
(CEN) committee on photocatalytic materials.