Author’s Accepted Manuscript
Molybdenum doped TiO 2 nanocomposite coatings:
visible light driven photocatalytic self-cleaning of
mineral substrates
B. Miljević, J.M. van der Bergh, S. Vučetić, D.
Lazar, J. Ranogajec
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Reference:
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http://dx.doi.org/10.1016/j.ceramint.2017.03.149
CERI14918
To appear in: Ceramics International
Received date: 23 February 2017
Revised date: 23 March 2017
Accepted date: 23 March 2017
Cite this article as: B. Miljević, J.M. van der Bergh, S. Vučetić, D. Lazar and J.
Ranogajec, Molybdenum doped TiO 2 nanocomposite coatings: visible light
driven photocatalytic self-cleaning of mineral substrates, Ceramics International,
http://dx.doi.org/10.1016/j.ceramint.2017.03.149
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Molybdenum doped TiO2 nanocomposite coatings: visible light driven
photocatalytic self-cleaning of mineral substrates
B. Miljevića,1 , J.M. van der Bergha, S. Vučetića, D. Lazarb, J. Ranogajeca
a
University of Novi Sad, Faculty of Technology, Bul. cara Lazara 1, 21000 Novi Sad,
Serbia
b
University of Novi Sad, Faculty of Sciences, Department of Physics, Trg Dositeja
Obradovića 4, 21000 Novi Sad, Serbia
Abstract
The molybdenum doped TiO2 nanocomposite layer double hydroxide (LDH)
suspensions, Mo:TiO2-LDHs, were synthesized by a wet impregnation method in order
to enhance the pure TiO2 (water suspension) photocatalytic activity and consequently its
self-cleaning efficiency under exposure to visible light. The aim was to produce
nanocomposites by a simple, energy saving and cost beneficial synthesis. The mass
ratio Mo/Ti was systematically varied (0.03, 0.06, 0.09, 0.12). The obtained
nanocomposite Mo:TiO2-LDH suspensions were first characterized by UV-Vis
spectroscopy (band-gap energies), Zeta-sizer (particle size distribution and stability) and
X-ray diffraction (XRD) (structure) and then applied onto the model mineral substrates,
brick and stone. The photocatalytic activity of the obtained coating was determined
based on the degradation kinetics of the Rhodamine B (RhB) under artificial visible
light irradiation (white LED). The obtained results were compared to the ones of the
unmodified TiO2-LDH suspension. The obtained results also showed that all prepared
Corresponding author, tel.: +381 21 4853623; fax: +381 21 450413.
E-mail address: miljevic@uns.ac.rs (Bojan Miljević)
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nanocomposites have good photocatalytic activity, particularly the suspension
Mo:TiO2-LDH with the Mo/Ti 0.03 mass ratio which possesses the best value. In
addition, as regards the visible light driven self-cleaning effect, this suspension has
proven to be a good protective functional coating for porous mineral substrates (bricks
and stones).
Keywords: B. Nanocomposites; C. Photocatalytic activity; D. TiO2; E. Functional
applications
1. Introduction
Recently, the attention of the scientific community dealing with environmental pollution
issues has been drawn by self-cleaning coatings and their commercial applications [1].
The researchers are mostly focused on hydrophilic photocatalytic coatings prepared
with anatase TiO2 which is the most used and the most efficient representative [1–5].
TiO2 is non-toxic and it has a high chemical stability, wide availability and relatively
low cost [2]. Pure anatase TiO2 has a wide band-gap energy of 3.2 eV [6–8] and it needs
UV irradiation in order to induce photocatalytic and hydrophilic phenomena and thus,
self-cleaning effect. Since UV fraction of the spectrum makes less than 5% of the
available solar light intensity, it is of a great importance to produce a visible light driven
photocatalyst with an enhanced photocatalytic activity. This would considerably extend
the range of TiO2’s possible industrial applications, not just in the field of
environmental contaminants degradation but also in the field of solar energy
conversion.
One of the possible ways for reducing the TiO2’s band-gap energy is to produce
a nanocomposite semiconductor photocatalyst by doping of TiO2 with cationic
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transition metals or metal-oxides. A promising element among them is molybdenum,
the dopant proposed by Grätzel and Howe [9] and subsequently used in the research of
numerous authors [2,3,7,10–22]. It is known that doping a material using metals with a
higher oxidation state (as Mo5+ and Mo6+) than that of the parental atom (Ti4+) increases
the photocatalytic activity. This is due to improved transfer and separation of photogenerated electrons and holes [13]. Grätzel reported that Mo6+ ion occupies interstitial
sites of the TiO2 matrix and behaves as an irreversible electron trap, while Mo5+ acts as
a reversible hole trap substitutional in the TiO2 matrix. The Mo6+ was chosen as a
dopant not only for its higher oxidation state than the parental Ti4+, but also because it
is not toxic [23–25] (especially in the form of a suspension). Additionally it possesses
good solubility, high availability and it is reasonably inexpensive. The improvement of
the photocatalytic activity seemed to be dependent on the concentration of the doping
cations [11]. However, there is a problem of balancing between the improved
photocatalytic activity and unwanted enhanced recombination of the charge carriers
which might occur due to higher absorption of light [26]. Although this fact has been
dealt with in literature, there is a huge discrepancy between different optimal
molybdenum contents reported. A group of researchers quotes the small values of the
optimal Mo concentration (e.g. 0.5-3%1 [7,9,10,13,17–21,26–28] ) and reports on the
limited solubility. Devi et al. reported on even smaller Mo concentrations, below 0.1%
[14,15]. On the other hand, there are reports by Kubacka et al. on relatively high Mo
concentrations (8-26% [16,22]) with >12% of solubility limit into the anatase structure.
What all the methods already used for synthesis of Mo-doped TiO2 nanocomposites
have in common, is a necessary energy input for heating or even cooling [19]. Most of
1
Authors refer on molybdenum content non-consistently, in three different ways: atomic percentage,
weight percentage and in molar percentage.
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the synthesis methods of the Mo-doped TiO2 reported in the literature used sol-gel
procedure with consequent calcination. This paper reports a rather simple and energy
saving synthesis of Mo-doped TiO2. It is later directly intercalated into the ZnAl-LDH
structure enabling its low cost commercial production and use for the coating of mineral
substrates.
In order to provide the best possible compatibility with the mineral substrates,
the obtained photocatalytically active molybdenum doped TiO2 described in this paper
was intercalated in the ZnAl-layered double hydroxide which possesses a structure
similar to clay minerals. Beside their unique nano-sheet structure, layered double
hydroxides (LDH) possess a very good compositional flexibility and controllable
particle size. Moreover, their low cost and easy manufacturing [29] make these
materials convenient for various engineering applications. Also, LDH structures
themselves have been proven as good redox catalysts [30,31]. In this study the obtained
nanocomposite Mo:TiO2-LDHs were applied on two model mineral substrates, bricks
and stones, in order to inspect its applicability on different types of materials, natural
(stone) and artificial (brick). Moreover, as these two substrate types have different pore
size distributions, the compatibility of the obtained Mo:TiO2-LDHs was studied in the
correlation with the substrate porosity. The developing of self-cleaning properties of
newly synthesized suspensions was monitored by the change of the contact angle [1]
with an increase of visible light irradiation exposure time.
2. Experimental procedures
2.1 Materials and synthesis
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A newly synthesized nanomaterial based on LDH (layered double hydroxides) and
photocatalytically active TiO2 particles altered with paramolybdate was obtained using a
modified low super saturation co-precipitation method [32,33]. The modified TiO2
particles were obtained by dissolving appropriate amounts of ammoniumparamolybdate in 10 mass% commercial TiO2 suspension (Evonik VP Disp. W 2730 X)
giving series of solutions with different Mo/Ti mass ratios: 0.03, 0.06, 0.09 and 0.12.
These solutions were added simultaneously into Zn and Al salts (4 ml min-1)
maintaining a constant pH value (using a mixture of NaOH and (NH4)2CO3) necessary
for LDH synthesis. The stabilization of the newly produced nanocomposite
(Mo:TiO2-LDH) was achieved by dilution and addition of a polyelectrolyte stabilizer
(ammonium-polyacrylate) [34]. The amount of the nanocomposite in diluted suspension
was 1 mass%. The synthesis was performed under the atmospheric pressure and at room
temperature.
The obtained nanocomposites (Mo:TiO2-LDH with different Mo/Ti mass ratios)
were firstly applied on the glass samples, and the suspension with the best
photocatalytic activity was further used for the application on the chosen brick and
stone mineral substrates. The nanocomposite suspensions were applied by spray
technique directly onto the glass samples/model substrates in 3 deposited layers with the
period of t = 5 min between two applications.
The chosen mineral substrates were bulk samples of natural stone and brick
samples prepared in laboratory conditions. The used stone samples are known as
Ptujska Gora sandstone from Jelovice quarry, in eastern Slovenia. The brick samples
were prepared by hand in a traditional way, using non-carbonate raw material mixture.
The dried brick models were fired in a laboratory kiln (2 hours at Tmax= 980 °C).
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2.2 Characterization of nanocomposites and mineral substrates
2.2.1 Particle size and colloid stability
The particle size distribution (PSD) and the colloid stability measurements of zetapotential were performed using the Malvern Instruments Zeta-nanoseries, model: Nano
ZS under the following conditions: refraction index of the investigated suspensions,
n= 2.61, refraction index of the dispersant (demineralized water) n0= 1.33, light
absorption = 0.3, suspension pH= 9.5. The PSD and the mean zeta potential results
were obtained as the average value after 12 scans had been performed.
2.2.2 Structural and compositional characterization by X-ray diffraction
The X-ray diffraction (XRD) measurements of the dried and powdered nanocomposite
suspensions and of the powdered mineral substrates were carried out using a Philips PW
1710 instrument, with Cu Kα1,2 radiation, and a step scan mode of 0.02° in the angular
range 2θ = (5–60)°. The exposition time at each point was 2 s. Bragg-Brentano
parafocusing geometry was used to increase the intensity and angular resolution. The
evaluation of the XRD patterns and their Rietveld refinement analysis were performed
using the PANalytical “HighScore Plus” software.
2.2.3 UV-Vis spectroscopy measurements
The absorbance of the newly synthesized Mo:TiO2-LDH nanocomposite suspensions
was measured by UV-VIS spectrophotometer Evolution 600, Thermo Scientific in the
range between 240 nm and 840 nm with the step of 1 nm and speed of 10 nm min-1.
Demineralized water was used as reference.
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The colour change of the substrates (non-carbonate brick and sandstone
samples) after the application of the chosen nanocomposite suspension (Mo/Ti mass
ratios: 0.03) was studied using the same UV-VIS spectrophotometer with the addition of
the DRA-EV-600 diffuse reflectance integrating sphere accessory. The evaluation of the
coated substrates optical parameters was done using softer “VL COLOR CALC”.
2.2.4 Measurements of photocatalytic activity
The photocatalytic behaviour was investigated in liquid phase [35] by the deposition of
the Mo:TiO2-LDH suspensions with the Mo/Ti mass ratios: 0, 0.03, 0.06, 0.09 and 0.12
onto the glass samples which were chosen as non-porous substrate models. The
suspension with the best value of the photocatalytic activity measurements on the glass
samples was further used for the application onto the mineral substrates (non-carbonate
brick and sand-stone samples).
According to the procedure adjusted to a porous substrate [35], the
photocatalytic activity of the coated mineral substrates was monitored using a
Rhodamine B (RhB) concentration change [4] under visible light irradiation. The
samples were irradiated for (30, 90, 150 and 210) min. and 24 h with a BRILIGHT white
LED visible light source (irradiance of 25 W·m-2). White LED source was used in order
to assure visible light irradiation without any UV light. The irradiance was measured
with Solar Light PMA2100 instrument using probe heads PMA2130 and PMA2110 for
visible and UV-A light, respectively. The same UV/VIS spectrophotometer which was
used for the colour change and absorbance measurements, was also used now in order
to carry out the monitoring of the RhB concentration change at the major absorption
peak at λ= 554 nm.
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2.2.5 Measurements of roughness and micro-hardness
In order to assess the influence of the chosen suspension (Mo:TiO2-LDH with the
Mo/Ti mass ratios 0.03) on the surface properties, the measurements of the roughness
and micro-hardness of the model substrates with and without coating were performed.
The surface roughness of the coated and non-coated mineral substrates was determined
with a precision device (Surtronic 25, Taylor Hobson) and the obtained data were
calculated applying ISO 4287 standard. The surface roughness was evaluated based on
the Ra parameter which represents the average roughness value of the five
measurements. The mechanical properties were determined by measuring the Vickers
microhardness (HV) with a microhardness tester model HVS 1000A, ZZV Precision
Tool Supply.
2.2.6 Substrate porosity measurements
Pore size distribution was measured with a mercury porosimeter (AutoPore IV 9500,
Micromeritics). Maximal intrusion pressure used was 228 MPa.
2.2.7 Contact angle measurements
The Surface Energy Evaluation System, Advex Instruments was used for the
measurements of the contact angle between the experimental fluid (glycerol) and the
coated surfaces of the investigated mineral substrates. Liquid drops, of about 5 μl in
volume, were gently deposited on the substrate surface by using a micro syringe. The
measurements of the initial contact angle (ci, after 1 s) were performed at five different
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points for each of the three specimens of the examined substrates. Each droplet
deposited onto the surface was measured five times. The contact angle values of the
coated and non-coated mineral substrates were monitored after visible light source
irradiation (under the same experimental conditions as in the case of photocatalytic
activity measurements).
3. Results and discussion
3.1 Colloid stability and particle size distribution
Figure 1. shows particle size distribution of the newly synthesized Mo:TiO2-LDH
nanocomposite suspensions. The sample with the Mo/Ti ratio of 0.09 has the most
uniform particle size diameter. All samples with molybdenum have narrower particle
size distributions than the sample without molybdenum (Fig. 1 - black). With the
increase of the Mo/Ti ratio (up to 0.09), a decreasing of the mean value of particle size
diameter was identified except in the case of the suspension with Mo/Ti ratio 0.12, due
to the agglomeration, where an increased value was obtained.
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Figure 1. The particle size distribution of Mo:TiO2-LDH nanocomposite suspensions
The zeta-potential was around -45 mV for all synthesized nanocomposite suspensions,
both for those with molybdenum as dopant and for the one without molybdenum
content which indicates a good colloid stability and a uniform distribution of the
particles within the colloid volume.
3.2 Structure and morphology characterization of nanocomposites
Figure 2. shows a comparison of the XRD patterns of the Mo:TiO2-LDH powders. The
intensity in arbitrary units was shifted up for clarification.
Figure 2. The powder X-ray diffraction patterns of the Mo:TiO2-LDHs systems
The identified crystal phases within the XRD pattern were the following: anatase-TiO2
(JCPDS No. 21-1272), rutile-TiO2 (JCPDS No. 89-4920), MoO3 (JCPDS No. 65-2421),
ZnAl-LDH (JCPDS No. 38-0486). All patterns show clearly unchanged positions of
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anatase (A) and rutile (R). MoO3 peaks are present in the case of the samples with larger
Mo content (Mo/Ti 0.09 and Mo/Ti 0.12) while they are absent in the case of the
samples with lower Mo content (Mo/Ti 0.03 and Mo/Ti 0.06) and the one without
molybdenum (Mo/Ti 0).
Thin films and multilayers exhibit thickness oscillations (so-called Kiessig
fringes [36]) in XRD spectra, especially in the region of low 2 values, close to the
reciprocal space origin and this phenomenon has been made use of in several methods
for investigation of layered type of materials [37–39]. Similar phenomenon was
observed in the samples with lower molybdenum content (Mo/Ti 0.03 and Mo/Ti 0.06)
and without molybdenum (Mo/Ti 0) which have broad features with 2 maxima at
5.81°, 12.4° and 18.99° (figure 2). These features appear periodically at a regular
distance of (2) = 6.59 corresponding to the length of d = 1.35 nm in the real space
(equation 1).
(1)
where Q denotes the difference of the scattering vectors Q in the reciprocal space.
That depends on the X-ray source wavelength , and on the Bragg’ angle as:
.
(2)
The determined value of d (1.35 nm) might be a nanosheet interlayer distance of the
Mo:TiO2-ZnAl-LDH systems. A similar value (d= 1.2 nm), determined with a high
resolution transmission electron microscopy was obtained for the TiO2-ZnCr-LDH
structure [29]. Moreover, a comparable value was also obtained by X-ray reflectivity
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(XRD -2 at low angles) in the case of a LDH structure with intercalated large
molecules in the existing interlayers [33].
Broad features, which are visible for low molybdenum content samples, are
absent in the cases of high molybdenum content samples. However, MoO3 pure oxides
are formed only in the samples with higher molybdenum content, which might indicate
that smaller quantity of molybdenum has gone through the intercalation. In the case of
lower Mo content, the pure oxide peaks are absent, but the interlayer thickness
oscillations are visible indicating that molybdenum was intercalated between the
ZnAl-LDH nanosheets before the oxidation could have occurred.
3.3 Band gap energies
Band gap energy Eg of the nanocomposite samples was determined using the Tauc’s
plot [40]. The method is based on the fact that the absorption of the light is dependent
on the band gap energy of the absorbing material (Kubelka-Munk theory) [41,42]. A
relation between the absorbance and the band gap energy Eg is given by [43]:
C(
)
(3)
with the h being a Planck’s constant, the frequency (linked to the measured
wavelength by = c/, c is the speed of light in vacuum) and C an energy-independent
constant. The factor n depends on the transition type, direct allowed (n=2) or indirect
allowed (n=1/2). According to the eq. 3, the band gap energy can be determined from a
plot of the modified absorbance
vs. the energy hν by extrapolating the linear
fit of the straight section to the =0 intercept of the energy coordinate. Figure 3.(a)
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shows the measured absorbance of the obtained nanocomposite Mo:TiO2-LDHs with
different molybdenum content, while figure 3.(b) presents a plot of the modified
absorption against the energy, according to the eq. 3. There is a reference of the
measurements of the pure commercial TiO2 in both figures. The band gap energy Eg
was calculated assuming the indirect transition (n=1/2) [8] for the prepared
Mo:TiO2-LDH nanocomposites and for pure titania as well.
(a)
(b)
Figure 3. The absorbance vs. wavelength (a) and the modified absorbance
plotted against the energy (b) measured for the Mo:TiO2-LDHs and for the pure TiO2.
The results presented in the table 1. show that the band gap energy of pure TiO2 is
3.22(6) eV, which is in a good agreement with the results reported in the literature for
anatase phase pure TiO2 (3.20 eV) [8]. The results determined for the Mo:TiO2-LDHs
show that the band energy decreases with the increase of the molybdenum content and
varies between 2.70 eV and 2.24 eV. This corresponds to the light emission
wavelengths between 458 nm and 554 nm covering a wide part of the visible fraction of
the electromagnetic spectrum.
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Table 1. Band gap energies of the pure titania and the synthetized Mo:TiO2-LDHs with
the corresponding wavelengths
Sample
pure TiO2
Mo/Ti 0
Mo/Ti 0.03
Mo/Ti 0.06
Mo/Ti 0.09
Mo/Ti 0.12
Eg (eV)
3.22(6)
2.66(3)
2.70(4)
2.56(2)
2.66(3)
2.24(1)
(nm)
385
466
458
485
466
554
Although TiO2-LDH (without any molybdenum) also exhibits the band gap
energy belonging to visible light (2.66 eV, 466 nm), it has to be considered with
reservation concerning the photocatalytic activity. This is clearly shown by our results
(Fig. 4) in the next section, where it is discussed further.
3.4 Photocatalytic activity
The photocatalytic activity Aeff was evaluated based on the efficiency of the RhB
degradation at the given absorption peak expressed by the equation as follows:
e
(4)
where C is the RhB concentration after a certain exposition time and C0 is the initial
RhB concentration. The results of the photocatalytic activity of the glass samples coated
with the suspensions of different Mo/Ti mass ratio are presented in the figure 4. The
obtained results confirm that all of the prepared suspensions have satisfying
photocatalytic activity (20% and above after 24 hours, Fig. 4).
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Figure 4. The photocatalytic activity of Mo:TiO2-LDH coatings on the glass substrates
using visible light as a source measured at different time.
The Mo:TiO2-LDH suspension with the Mo/Ti mass ratio 0.03 showed the best
photocatalytic activity (about 35% after 24h). For the suspensions with the larger
molybdenum content (Mo/Ti mass ratios 0.06, 0.0.9 and 0.12) the photocatalytic
activity values are lower than for the TiO2-LDH suspension.
What is significant here is the fact that not only does the band gap energy
decrease with the increase of molybdenum content (Tab. 1), but this also enables more
intense electron-hole recombination and thus the suppression of the photocatalytic
activity [44]. The mechanism of recombination in heterogeneous photocatalysis has not
yet been completely understood [45]. Despite significant improvement of visible light
absorption properties, only a small increase of visible light activity has been observed
[44,46] in attempts to produce more efficient TiO2 nanowires. The interplay between
visible light photo-induced generation of electron-hole pairs and their recombination, in
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our case study, revealed the sample with Mo/Ti mass ratio of 0.03 as the most
photocatalytically active one. A possible explanation why Mo:TiO2-LDH 0.03
properties prevailed in comparison to the one of TiO2-LDH could be that the indirect
recombination in the system with molybdenum is slower. This is due to the donor level
which is formed in the band gap of TiO2 between conduction band and Fermi level [45]
by doping with molybdenum.
Based on the fact that the glass samples coated with Mo:TiO2-LDH 0.03 possess
the highest values of the photocatalytic activity, this suspension was further used for the
application on the mineral substrates (brick and stone samples).
3.5 Properties of mineral substrates
3.5.1. Phase composition and porosity of the mineral substrates
The XRD patterns of the measured substrates are shown in figure 5. The intensity of the
diffraction measured on the stone sample was shifted to the higher values in arbitrary
units for better clarity. In the case of stone sample (black line and dots), quartz (Q),
calcite (C), dolomite (D), mica (M), feldspar (F), but also hematite (H) and chamosite
(Ch) were identified. For the brick sample only quartz, feldspar and hematite were
present confirming a typical composition (Fig. 5, red line and dots) for bricks produced
from clayey materials free of carbonates.
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Figure 5. The powder XRD patterns of the measured mineral substrates, stone (black)
and brick (red) with the identified mineral phases
The obtained results of the textural analysis (Fig. 6) reveal the stone models as samples
with relatively low total porosity, estimated around 13%. This value is 25% in the case
of the brick models, which is approximately two times higher. Considering the fact that
the brick samples are non-carbonate systems, higher values of the total porosity is the
consequence of their production (traditional, handmade). Moreover, the difference in
the origin of the two kinds of materials (natural stone and artificial brick) is also
reflected on the pore size distribution. In the case of the stone samples, the dominant
pore radius is in the range of (1-2) m, while in the case of the brick samples (Fig. 7)
the dominant pore radius is in the range of (0.5-1) m.
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Pore voulme fraction (%)
25.00
Stone
20.00
15.00
10.00
5.00
0.00
Pore diameter (μm)
Figure 6. Pore size distribution of the stone mineral substrate
Pore volume fraction (%)
50.00
Brick
40.00
30.00
20.00
10.00
0.00
Pore diameter (μm)
Figure 7. Pore size distribution of the brick mineral substrate
3.6 Functional properties of the coated mineral substrates
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In order to obtain the effect of the addition of molybdenum, during the synthesis, on the
functional properties of the mineral substrates, the following groups of samples were
examined: mineral substrates without coating, mineral substrates coated with the
TiO2-LDH (without addition of molybdenum) and the mineral substrates coated with
Mo:TiO2-LDH (Mo/Ti mass ratio of 0.03).
3.6.1 Surface properties of mineral substrates
The results of the surface characterization performed by measuring the Vickers
microhardness values (HV) and the roughness parameters (Ra) before and after the
application of the chosen suspensions remain almost the same. This suggested no
significant influence of the suspension application on the surface characteristics.
Considering the possible industrial application, one of the most important
characteristics of the coating applied on mineral substrates is the surface colour change,
which should be as low as possible. Calculations of colour differences were performed
using CIE (Commission international de l`Eclairage) L*a*b* relative to a white
background. The L* parameter corresponds to the degree of lightness and darkness,
whereas a* and b* coordinates correspond to red or green (+a* = red, a* = green) and
yellow or blue (+b* = yellow, b* = blue), respectively. The spectrophotometer was
calibrated with a standard white plate made o “Spectralon” material. Total colour
differences before and after the application of the nanocomposite suspensions were
calculated as follows:
(5)
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where ∆L*, ∆a* and ∆b* are the di erences in the respective values be ore and after
the application of coatings [47].
Table 2. The total colour di erence (ΔE) of the coated mineral substrates
Coating
TiO2-LDH
Mo (0.03)TiO2-LDH
Stone
0.83
0.98
Brick
0.95
0.94
Sample
The values of the total colour difference (Tab. 2) after the application of the
photocatalytic suspensions by spray technique, are minor and are identified as very low
(∆E*<1). The obtained values of colour difference indicate a low risk of chromatic
incompatibility before and after the application of the photocatalytic suspension.
Evidently, the existence of high level of compatibility of the newly designed suspension
with the used mineral substrates is proved.
3.6.2. Self-cleaning effect of the coated mineral substrates
The photocatalytic activity of the coated mineral substrates as the function of visible
light irradiation time is given in figure 8. Considering the presented results, good
photocatalytic properties of the coated mineral substrates are obtained. In the case of
brick mineral substrates the chosen suspension has stronger impact on the photocatalytic
activity value compared with that on the stone samples. This could be the consequence
of higher porosity which might initiate an increase of the development of the pore
network of active sites at the surface of the brick samples (Fig. 6 and Fig. 7).
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Figure 8. Photocatalytic activity of the coated mineral substrates as the function of
visible light irradiation time
(a)
(b)
Figure 9. Contact angle (θci) of the coated and non-coated mineral substrates: (a) brick
and (b) stone as a function of visible light irradiation time
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The results of the contact angle measurements (Fig. 9) indicate that the application of
the developed suspension (Mo (0.03)-TiO2-LDH) leads to the decreasing of the contact
angle. For the brick samples (Fig. 9 (a)), the hydrophobic surface of non-coated mineral
substrate (θci 105°) switched into the hydrophilic surface for the coated surface
(θci 87°) after 24h of visible light irradiation (Fig. 10). In the case of the stone sample
(Fig. 9 (b)), the non-coated hydrophilic surface (θci 58°) became more hydrophilic
(θci 36°) after coating. These results proved an improvement of the photocatalytic
properties after the application of the developed suspension. Moreover, with the
increased irradiation time (visible light source) in the case of all performed
measurements, the contact angle values constantly decreased. These results directly
prove that by the application of the newly developed suspension good self-cleaning
properties of the coated mineral substrates under the visible light irradiation are
obtained.
Figure 10. Contact angle (θci) measurements of the non-coated and coated mineral
substrates, stone (top) and brick (bottom) after 0h and 24h of visible light irradiation
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Conclusion
The inorganic-inorganic nanocomposites, based on layered double hydroxides (LDHs)
associated with the photocatalytically active molybdenum doped TiO2 were synthesized
and characterized. In order to investigate possible applicability, the composite with the
best properties considering functionality was applied on mineral substrates: natural
stone and artificial non-carbonate brick samples.
To the best of the authors’ knowledge, it was the first time that molybdenum as a
dopant for TiO2, intercalated in layer double hydroxide, was used with the aim to
improve its visible light driven photocatalytic activity and, consequently, to enhance its
self-cleaning efficiency.
The newly synthesized nanocomposite suspensions (with the Mo/Ti mass ratio 0,
0.03, 0.06, 0.09, 0.12) were characterized as stable nano-suspensions (zeta potential
-45 mV) with the uniform particle size distribution. The powder XRD study revealed
that the photocatalytically active Mo:TiO2 is intercalated into ZnAl-LDHs for the lower
molybdenum content (Mo/Ti 0, 0.03, 0.06) whereas for the content higher than
9 mass%, a molybdenum oxide is formed. This indicates a possibility that the
intercalation is less successful for higher concentrations. The existence of broad XRD
features with the systematic periodical appearance indicates that the intercalation of
Mo:TiO2 into the LDH structure was successful.
In the experiment, the band gap energy decreased with the molybdenum content
for all of the prepared nanocomposites, in comparison with the pure TiO2. Moreover,
the obtained results of the band gap energies correspond to the light emission
wavelengths covering a wide part of the visible fraction of electromagnetic spectrum
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(458 nm-554 nm) giving the basis for the expectation of the visible light driven
photocatalytic properties of the prepared nanocomposites. The measurements of the
photocatalytic properties of the glass samples coated with the prepared nanocomposites
proved good visible light photocatalytic activity (more than 20% after 24h) for all of the
suspensions. The same measurements indicated that the nanocomposite with the Mo/Ti
0.03 mass ratio possesses the highest value of the photocatalytic activity and it was
further used for the application on the mineral substrates. Good visible light driven
photocatalytic activity of the mineral substrates (both, brick and stone) coated with the
nanocomposite (Mo/Ti 0.03 mass ratio LDH) was also confirmed. Additionally, the
contact angle values of the coated mineral substrates decreased with the irradiation time
and the self-cleaning properties of the developed nanocomposite were proved.
As regards the aesthetical appearance, the newly developed nanocomposite
(Mo/Ti mass ratio 0.03) shows very good transparency properties without significant
influence on the surface colour which is a necessary factor for general application.
In view of all the presented results it could be concluded that the developed
product proved noticeably promising regarding the simplicity of the energetically
beneficial production protocol, the aesthetical appearance, visible driven photocatalytic
effect and self-cleaning properties. Regarding long-term photocatalytic applications of
this product on porous building materials, a further durability assessment is needed.
Acknowledgments
The authors are grateful for the support of the Ministry of Education, Science and
Technological Development of the Republic of Serbia (Project number: III 45008).
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