# Electrophoretic Deposition of SnO2 Nanoparticles and Its LPG Sensing Characteristics

Authors: Göktuğ Günkaya; Mevlüt Gürbüz; Aydın Doğan
Journal: Journal of Sensors
 (2015)

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## Abstract

HomogenizedSnO
2 nanoparticles (60 nm) in acetylacetone mediums, both with and without iodine, were deposited onto platinum coated alumina substrate and interdigital electrodes using the electrophoretic deposition (EPD) method for gas sensor applications. Homogeneous and porous film layers were processed and analyzed at various coating times and voltages. The structure of the deposited films was characterized by a scanning electron microscopy (SEM). The gas sensing properties of the SnO
2 films were investigated using liquid petroleum gas (LPG) for various lower explosive limits (LEL). The results showed that porous, crack-free, and homogeneous SnO
2 films were achieved for 5 and 15 sec at 100 and 150 V EPD parameters using an iodine-free acetylacetone based SnO
2 suspension. The optimum sintering for the deposited SnO
2 nanoparticles was observed at 500°C for 5 min. The results showed that the sensitivity of the films was increased with the operating temperature. The coated films with EPD demonstrated a better sensitivity for the 20 LEL LPG concentrations at a 450°C operating temperature. The maximum sensitivity of the SnO
2 sensors at 450°C to 20 LEL LPG was 30.


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## Body

## 1. Introduction

The leakage of the LPG, NO2, SO2, CO, H2, and H2S has a detrimental effect on human health and the environment during production, storage, transportation, and usage stages, due to their toxic and irritating nature [1–3]. Some semiconductor oxides such as TiO2, ZnO, WO3, and SnO2 are the most widely used to detect toxic and explosive gases [4]. SnO2 is one of the most studied semiconductor oxides among these materials because of its n-type large band gap (3.6 eV) and good quality optical and electrochemical properties [5–8]. SnO2 is widely used in transparent conducting electrodes, dye-sensitized solar cells, catalytic support materials, high-capacity lithium-storage, electrochemical or photo electrochemical based energy conversions, and gas sensor applications [7–9]. SnO2 nanoparticles are used for gas sensing applications in particular because of their relatively low operating temperature, simplicity, small dimensions, low cost, high reliability, high surface area, and easy adsorption of oxygen on its surface [10–14]. These properties lead to a high capability in detecting combustible gases such as methane, CH4, carbon monoxide CO, LPG, and NO2 [5, 15, 16].There are various film fabrication technologies that are used to overcome difficulties in sensing applications. Different sensing properties are observed by changing the grain size, film thickness, and porosity of the sensing material. For example, CO and CH4 can penetrate; hence, both react to the oxygen on the inner SnO2 grain boundary surfaces. If this was not the case, the other gases such as ethanol, densify on the film surface. The selectivity can be adjusted by controlling the porosity and thickness between the film surface and the electrical contacts [6–8]. A number of coating techniques such as physical vapor deposition (PVD), chemical vapor deposition (CVD), plasma spraying, tape casting, slip casting, thick film screening, and EPD have been published for the deposition of SnO2 films [17, 18]. EPD has some advantages such as possessing a simple setup, ambient atmosphere operation, and easy control of the composition and morphologies of the deposited layer when compared to other film deposition techniques [19]. Also, a wide range of thickness from the nanometer to the micrometer scale on curved, rough, or plain (smooth) surfaces is fabricated with EPD. A more uniform and reliable porous ceramic film structure can be easily fabricated by EPD [20]. The EPD technique is based on the movement of the charged particles through the application of an external electric field in the colloidal stable suspension [21]. EPD is defined by two processes: electrophoresis and deposition. Electrophoresis is the migration of the particles under an electric field, whereas deposition refers to the bonding of the moved particles on the desired areas such as the substrate surface and size and size distribution of the ceramic powder, suspension properties, deposition time, and the applied voltage are the main critical parameters to control the film microstructure for EPD [22].Functional ceramic films such as SiC, ZrO2, YSZ, ZnO, TiO2, and SnO2 have been fabricated with EPD in the field of corrosion resistant layers, electrical insulation, thermal barrier layers, solar cells, sensors, photocatalysts, wear-resistant layers, and optical and structural devices [23–27]. EPD of crack-free magnesium oxide coated SnO2 films for dye-sensitized solar cells was published by Li et al. Nearly 140 μm of magnesium oxide coated SnO2 film thickness was successively achieved on FTO glass from colloidal SnO2 (7 nm) suspension. The photoelectric conversion efficiency above 7% was enhanced for various Mg/Sn ratios [28]. Ui et al. used EPD for lithium secondary batteries using binder-free commercial SnO2 nanoparticles. They clarified that EPD coated SnO2 films were effectively operated as the negative electrode for lithium batteries [29]. EPD fabricated SnO2 films from Sn metal powder for nitrogen dioxide gas detection at low temperatures were reported by Liu et al. They present that the sensing of the sensor to NO2 gas increased with increasing operating temperature and gas concentration [30]. EPD of the SnO2 commercial powder to sense CO, O2, and H2 gas was published by Gardeshzadeh et al. [31, 32]. They have just concentrated on current-time variations for CO, O2, and H2 gas. LPG is the most popular flammable and explosive gas; therefore detection of LPG leakage is extremely important to prevent fatal events and damage to the environment [33]. In literature, the number of studies on the SnO2 coated surface with the EPD for LPG sensing is quite low.As stated above, some reports on SnO2 sensors fabricated with EPD are available to sense LPG. Therefore, the aim of this study is to deposit porous and homogenous SnO2 films using EPD. Also, the effect of the EPD coating process on the structural, surface morphological, and LPG sensing properties of the SnO2 films was studied.


## 2. Experimental Procedure

### 2.1.  Stabilization of SnO2 Nanoparticles for EPD

In our study, Malvern Nano ZS was used to determine particle size distribution and zeta potential of the SnO2 solutions using dynamic light scattering. It measures particle size distributions by measuring the angular variation in intensity of light scattered as a laser beam passes through a dispersed and stabile particulate sample. Approximately a 60 nm (17.70 m2/gr) in average particle size SnO2 nanopowder was provided from MTI Corp. Two different types of EPD suspensions were prepared in order to compare coating parameters. The first EPD suspension was including iodine (I
2) while in the second one it was without iodine. The first EPD suspension was prepared by mixing SnO2 with I
2 added acetylacetone (AcAcI). Optimum concentration of the suspension was 50
g
r
S
n
O
2
/
L
A
c
A
c
I. Ultrasonic homogenization was applied to break the agglomerates at 20 watts for 15 minutes. Malvern Nano ZS and sedimentation tests were used to obtain the optimum amount of iodine for stabilization of SnO2 in acetylacetone (AcAc) and zeta potential measurements. The second EPD suspension was prepared in the same manner in AcAc without iodine. Ultrasonic homogenization at 20 watts for 4 min was applied to disperse the SnO2 nanoparticles.


### 2.2. Substrate Preparation and Coating of SnO2 Using EPD

EPD is a colloidal process based on the motion of charged droplets and particles in a suspension toward an electrode of the opposite charge under an applied DC electric field. Our previous study gives the detailed schematic view of EPD unit. When the electric field is applied to a homogenized suspension surface charged particles migrate toward and away from the charged electrode, and SnO2 particles accumulate on interdigital electrodes [34]. Figure 1(a) gives the schematic view of interdigital electrode and sensor design. As given in Figures 1(b) and 1(c) sensing element (interdigital electrodes) and heater (back side) were screen printed with Pt paste on the alumina substrates. EPD unit was vertically designed and electrode at the vertical top of the system was used as cathode (coated layer, interdigital electrode). A platinum-palladium (Pt-Pd) sheet was used as counter electrode (anode). Cathode was fabricated Pt coated alumina (Coorstek ADS 996) with 1.2 cm × 1.2 cm surface area. Pt paste for conductive substrate was applied to the surface by brushing, and the second layer was obtained by screen printing. Then, Pt coated alumina substrate was dried in an oven at 130°C for 15 minutes and then sintered at various temperatures for 5, 10, 15, and 20 minutes. At different voltages (50 V–150 V) with various ranges between electrodes (10 mm, 15 mm, and 20 mm) and depositing time (5 sec–120 sec), parameters were experimentally selected for the optimization of the electrophoretic deposition process.Figure 1
Schematic view (a), front side (b), and back side (heater) (c) of the sensor.
(a)
(b)
(c)


### 2.3. Sintering and Characterization of EPD Deposited SnO2 Films

SnO2 deposited substrates were sintered at a temperature within the range of 300°C and 600°C for 15 minutes in an ambient atmosphere. The film thickness and the microstructures of both the sintered and unsintered SnO2 layers were examined by a scanning electron microscope (SEM, ZEISS Supra VP 50). The gold-palladium thin film was applied with a sputtering on the top and side surface of the SnO2 film in order to avoid charging during the SEM characterization.


## 2.1.  Stabilization of SnO2 Nanoparticles for EPD

In our study, Malvern Nano ZS was used to determine particle size distribution and zeta potential of the SnO2 solutions using dynamic light scattering. It measures particle size distributions by measuring the angular variation in intensity of light scattered as a laser beam passes through a dispersed and stabile particulate sample. Approximately a 60 nm (17.70 m2/gr) in average particle size SnO2 nanopowder was provided from MTI Corp. Two different types of EPD suspensions were prepared in order to compare coating parameters. The first EPD suspension was including iodine (I
2) while in the second one it was without iodine. The first EPD suspension was prepared by mixing SnO2 with I
2 added acetylacetone (AcAcI). Optimum concentration of the suspension was 50
g
r
S
n
O
2
/
L
A
c
A
c
I. Ultrasonic homogenization was applied to break the agglomerates at 20 watts for 15 minutes. Malvern Nano ZS and sedimentation tests were used to obtain the optimum amount of iodine for stabilization of SnO2 in acetylacetone (AcAc) and zeta potential measurements. The second EPD suspension was prepared in the same manner in AcAc without iodine. Ultrasonic homogenization at 20 watts for 4 min was applied to disperse the SnO2 nanoparticles.


## 2.2. Substrate Preparation and Coating of SnO2 Using EPD

EPD is a colloidal process based on the motion of charged droplets and particles in a suspension toward an electrode of the opposite charge under an applied DC electric field. Our previous study gives the detailed schematic view of EPD unit. When the electric field is applied to a homogenized suspension surface charged particles migrate toward and away from the charged electrode, and SnO2 particles accumulate on interdigital electrodes [34]. Figure 1(a) gives the schematic view of interdigital electrode and sensor design. As given in Figures 1(b) and 1(c) sensing element (interdigital electrodes) and heater (back side) were screen printed with Pt paste on the alumina substrates. EPD unit was vertically designed and electrode at the vertical top of the system was used as cathode (coated layer, interdigital electrode). A platinum-palladium (Pt-Pd) sheet was used as counter electrode (anode). Cathode was fabricated Pt coated alumina (Coorstek ADS 996) with 1.2 cm × 1.2 cm surface area. Pt paste for conductive substrate was applied to the surface by brushing, and the second layer was obtained by screen printing. Then, Pt coated alumina substrate was dried in an oven at 130°C for 15 minutes and then sintered at various temperatures for 5, 10, 15, and 20 minutes. At different voltages (50 V–150 V) with various ranges between electrodes (10 mm, 15 mm, and 20 mm) and depositing time (5 sec–120 sec), parameters were experimentally selected for the optimization of the electrophoretic deposition process.Figure 1
Schematic view (a), front side (b), and back side (heater) (c) of the sensor.
(a)
(b)
(c)


## 2.3. Sintering and Characterization of EPD Deposited SnO2 Films

SnO2 deposited substrates were sintered at a temperature within the range of 300°C and 600°C for 15 minutes in an ambient atmosphere. The film thickness and the microstructures of both the sintered and unsintered SnO2 layers were examined by a scanning electron microscope (SEM, ZEISS Supra VP 50). The gold-palladium thin film was applied with a sputtering on the top and side surface of the SnO2 film in order to avoid charging during the SEM characterization.


## 3. Results and Discussion

### 3.1. Stabilization of SnO2 Nanoparticles for EPD

The effect of the various mediums such as acetylacetone, isopropyl alcohol, and ethanol was experimentally investigated in order to stabilize the SnO2 nanopowder. Table 1 gives the zeta potential and conductivity of the suspensions. As given in the table, zeta potential and conductivity have a critical role for stabilization and EPD coating. Ethanol has very low zeta potential; therefore the particle is easily precipitated. Isopropyl alcohol has better zeta potential but its conductivity is very poor when compared to other solvents. Therefore migration of the particle is very low. On the other hand acetyl acetone has nearly 30 mV zeta potential and 0,00149 μS/cm conductivity. These values are enough for stabilization and effective EPD coating. The sedimentation tests showed that the best stabilization for the SnO2 was provided using the acetyl acetone (AcAc) medium. Figure 2 shows the sedimentation test for the SnO2 particles in both the iodine added and iodine-free AcAc suspension. As shown in Figure 3, the stability of the AcAc based SnO2 suspension was improved with the iodine addition. The zeta potential value plays a vital role in determining the surface charge of the particles introduced by the zeta potential. Figure 3 shows that zeta potential graph of SnO2 particles in AcAc based suspension changes from negative to zero up to 0.42 g/L iodine concentration. After this point, it increases zero to positive by changing the amount of iodine. The zeta potential has maximum value (nearly 35 mV) for 0.7 gr/L iodine concentration. Both zeta potential and sedimentation experiments show that stabilization and well-dispersed suspension are achieved by iodine addition. Iodine is used to positively charge the ceramic particles. As given reaction, protons are formed: (1)
C
H
3
C
O
C
H
2
C
O
C
H
3
+
2
I
2
⟷
I
C
H
2
C
O
C
H
2
C
O
C
H
2
I
+
2
I
-
+
2
H
+The iodine reaction between an organic solvent and its alkyls groups creates some ions which is the cause of increasing the suspension conductivity. Therefore, conductivity of acetyl acetone based suspension is much larger than other solvents. This larger conductivity with increasing iodine causes the increase of the zeta potential of ceramic suspension [35, 36].Table 1
Zeta potential and conductivity of suspensions in three solvent media.
Suspension media
Zeta potential (mV)
Conductivity (μS/cm)
Ethanol
−5.6
0.117
Acetyl acetone
+29
0.00149
Isopropyl alcohol
+55
0.0009Figure 2
Sedimentation test of SnO2 nanoparticles in iodine added AcAc and AcAc mediums: iodine added AcAc suspension at the beginning of sedimentation test (a), iodine added AcAc suspension after 24 hours (b), suspension without iodine beginning (c), and suspension without iodine after 24 hours (d).
(a)
(b)
(c)
(d)Figure 3
Zeta potential of SnO2 nanopowder in iodine added acetyl acetone medium.The evaporation of the iodine from coating layer is a rapid process, but there are still some doubts that it is purified completely. It can cause undesirable reaction and impurity during sensor application. It may act as a contaminant; hence sensor sensitivity or accuracy can change unexpectedly. For this reason, the optimization of the suspension in the absence of iodine is necessary. Because of the probable iodine effect, another suspension was prepared without iodine. The process of the suspension focused on ultrasonic dispersion in this stage. The optimization of the ultrasonic sonification was performed at various times, and power combination was used to enhance the stabilization. The optimum values for the stabilization of the suspension were observed as 20 W and 4 min. The ultrasonic sonification power and time are significant in order to minimize the agglomeration of the particles in the suspension. Excess time and ultrasonic power cause an increase in agglomeration. However, less dispersion time and ultrasonic power combination may cause the insufficient dispersion of the agglomerates. Therefore, the dispersion of the nanosized powder, especially under 100 nm, is very difficult due to the electrostatic attractive forces between the particles [37]. Figures 4(a) and 4(b) show the particle size distribution of the SnO2 nanopowders. Figure 4(a) displays the trimodel size distribution of suspension prior to the ultrasonic homogenizations process due to agglomeration. However, Figure 4(b) presents the monomodel and the narrow particle size distribution after ultrasonic homogenization. The particle size distribution of the SnO2 in the AcAc without iodine was approximately 100 nm.Figure 4
Size distribution of SnO2 nanopowder in AcAc medium before (a) and after optimum ultrasonic homogenization (b).
(a)
(b)


### 3.2. Electrophoretic Deposition of SnO2 Nanopowder

#### 3.2.1. EPD in Iodine Added AcAc Based SnO2 Suspension (Process 1)

The electrophoretic deposition was performed between 50 and 150 V using AcAcI suspensions. The electrodes’ distance and depositing time were 1 cm and 30 sec, 60 sec, 90 sec, and 120 sec, respectively. The optimum deposition voltages were 100 V and 150 V for the SnO2 accumulation on the interdigital electrodes. The coating quality was adversely affected by either increasing or decreasing the deposition voltage. When the three different deposition voltages were compared, the most homogeneous coating was obtained at 100 V. Figure 5 shows that the migration of the SnO2 nanopowder at 100 V was higher than the others and resulted in higher deposition yield on any coating surface. Both 50 V and 100 V series have better coating results when compared to 150 V. Migration control of the particles becomes more difficult at higher voltage (150 V). Therefore, suspension concentration between electrodes decreases rapidly, and this causes a decrease in deposition weight.Figure 5
EPD of SnO2 nanoparticles in AcAcI medium at various voltages (50-100-150 V) and deposition time (30-60-90-120 sec).


#### 3.2.2. EPD in AcAc Based SnO2 Suspension without Iodine (Process 2)

The electrophoretic deposition of the SnO2 nanopowder in the AcAc medium was successfully achieved between 100 and 150 V for a 1 cm electrode distance and various deposition times (5 sec–60 sec). As given in Figure 6, 150 V was the optimum voltage for the SnO2 deposition when compared to 100 V. As expected, the coating yield increased with deposition time for each coating voltage.Figure 6
EPD of SnO2 nanoparticles in AcAc medium at various voltages (100-150 V) and deposition time (5-15-30-45-60 sec).When compared, the EPD of the SnO2 nanopowder in the AcAc with iodine and the surface charge of the particles in the AcAcI suspension were higher than the AcAc suspension. There was no sedimentation at 24 hours in the AcAcI suspension from the sedimentation test, but nearly 5.4% of the AcAc suspension was precipitated (Figure 2). However, the migration of the SnO2 particles in the pure AcAc suspension was higher than iodine added suspension even if it has a higher surface charge. It could be explained that the increase of ionic concentration has adverse effect on double layer. Therefore, it causes the reduction of SnO2 migration during EPD [22]. The weight of EPD coating obtained at 150 V for 30 sec is nearly 0.006 gr/cm2 (6 times higher than process 1). Therefore, process 2 is more convenient for sensor applications. Also, creating a homogeneous film coating in a short coating time was the main purpose of this study. Therefore, shorter deposition times were investigated for AcAc based suspension. Efficient deposition at 100 V and 150 V for 5 sec and 15 sec produced a homogeneous SnO2 layer.


#### 3.2.3.  Sintering of Coated SnO2 Nanopowder with EPD

Porosity, homogeneity, high surface area, and small grain size are the main desired properties of the sensor for increasing the adsorption into certain gases [38]. Because of this reason, a heat treatment should be applied only for the neck formation between the particles in order to enhance the mechanical properties of the deposited layer. Therefore, the microstructure of the deposited SnO2 films is controllable by the sintering temperature. Nanosized powders possess high surface energy due to their high surface area. The surface energy is the driving force for the sintering. Therefore, nanopowders can be sintered at a low sintering temperature for a shorter sintering time. The sintering temperature range of the SnO2 commercial powder fluctuates between 1000 and 1400°C, but the nanosized powder is processed at a lower sintering temperature due to its high surface energy [39, 40]. The aim at the sintering step is to determine the neck formation temperature between the SnO2 nanopowders. The surface diffusion is the dominant sintering (mass transport) mechanism for the SnO2 within a range of 500–1000°C [39]. Figures 7(a)–7(e) give the sintering behavior of the deposited SnO2 nanopowders at various temperatures. As the given figure, no neck formation was observed below 500°C (Figures 7(a)–7(c)). The neck formation between the SnO2 nanopowders was seen at 500°C and 600°C (Figures 7(d) and 7(e)). The SEM investigations showed that the homogeneous SnO2 film layer was achieved by the EPD on the Pt coated alumina substrate. The film thickness was approximately 6 μm (Figure 7(f)).Figure 7
SEM images of unsintered SnO2 (a), sintered SnO2 at 300°C-400-500-600°C for 5 minutes (b–e), and side view of film thickness (f).
(a)
Unsintered
(b)
300°C
(c)
400°C
(d)
500°C
(e)
600°C
(f)
Side view of SnO2 film


#### 3.2.4. Gas Sensing Analyses of the Deposited SnO2 Films with EPD

Gas sensitivity can be controlled by the surface area and the particle size. The driving force was the high surface area and small pores in the range of the micropore or mesopore in the film structure using the nanopowder in the gas sensing applications. The sensing mechanisms of the gas sensors explained the surface reactions of the semiconducting oxide with hazardous gases. The LPG sensing performance tested the change in the resistance of the SnO2 film in the presence of the gases. When the sensor was exposed to the toxic and explosive gases, two reactions occurred on the film surface. The first reaction was the oxygen molecules in air which were physisorbed on the surface sites. They were ionized when taking an electron from the conduction band of the semiconductor. Therefore, the resistance of the gas sensors increases. When the semiconductor oxide sensor is exposed to the reducing gases, it reacts with chemisorbed oxygen. Releasing the trapped electron back to the conduction band, it causes a decrease in the resistance of the semiconductor oxide sensor [41, 42]. As given in Figure 7, the diameter of the nanopowders was smaller than 100 nm, and their pores were below 50 nm. These investigations showed that the deposited layers can be used for LPG sensing.As well as being used as domestic, commercial, and industrial fuel, it also has an area of use in the automobile sector under the name of autogas [43, 44]. The lowest explosive limit (LEL) is the minimum gas concentration that causes combustion in the air in the presence of an ignition source. The gas leakage concentration should not exceed 20% LEL (<3000 ppm) for safety reasons. Liquefied petroleum gas (LPG) was used for gas sensing experiments. The EPD deposited SnO2 sensors were placed in a cylindrical chamber (≈3 liter). The test chamber was designed to allow the circulation of the air and gas. The gas sensing measurement was performed between 250°C and 450°C for various LEL concentrations. The sensitivity of the SnO2 films was determined as S
=
R
a
/
R
g, where R
a was the resistance of the sensor in the presence of air and R
g was the resistance in the presence of the LPG [41, 45]. The resistance measurements were analyzed with the KEITHLEY 2410-C multimeter.Figures8(a) and 8(b) present the sensing results of the SnO2 sensors. Figure 8(a) shows the sensitivity variation of the SnO2 sensor as a function of the LPG concentration in the range of 10–100 LEL at different operational temperatures, namely, 300, 350, 400, and 450°C. It was observed that the sensitivity of the sensor increases along with the increasing operation temperature for all the LPG gas concentrations. These results follow a similar trend to Majumder et. al’s study, which was related to SnO2/Pd composite films deposited on the Si/SiO2 substrates with sputtering [46]. The best sensor sensitivity was observed at 450°C for all the LPG concentration. Moreover, the sensor sensitivity to the 20 and 30 LEL LPG sharply increases above the 350°C operation temperature (Figure 8(b)). It could be related to the presence of more stable adsorbed oxygen depending on the heat treatment after the coating.Figure 8
Sensitivity of fabricated SnO2 sensor with EPD: (a) for various LPG concentrations at various operating temperatures and (b) sensitivity to 20 and 30 LEL LPG at various operating temperatures.
(a)
(b)In our previous studies we have reported that the sensitivity of electrospray deposited (ESD) sensors was between 1.1 and 2.51 for 20 LEL LPG concentration [2]. The sensitivity of sensors produced by EPD at same LPG concentration was between 12 and 30. As a result, the sensitivity of EPD coated SnO2 sensors was nearly twelve times greater than ESD coated SnO2 sensors due to their highly porous structure and larger quantity of powder accumulation. According to our approach, more porous and thicker films can be produced by high deposition voltage, short deposition period, and short distance between electrodes. These were led to increase in the interaction of the particles during migration when the electric field was applied. In this case, individual particles were tended to agglomerate during EPD. These agglomerated particles were created by looser packing and thicker and more porous coating. Consequently, EPD fabricated SnO2 sensors had higher sensitivity than ESD fabricated sensors.


## 3.1. Stabilization of SnO2 Nanoparticles for EPD

The effect of the various mediums such as acetylacetone, isopropyl alcohol, and ethanol was experimentally investigated in order to stabilize the SnO2 nanopowder. Table 1 gives the zeta potential and conductivity of the suspensions. As given in the table, zeta potential and conductivity have a critical role for stabilization and EPD coating. Ethanol has very low zeta potential; therefore the particle is easily precipitated. Isopropyl alcohol has better zeta potential but its conductivity is very poor when compared to other solvents. Therefore migration of the particle is very low. On the other hand acetyl acetone has nearly 30 mV zeta potential and 0,00149 μS/cm conductivity. These values are enough for stabilization and effective EPD coating. The sedimentation tests showed that the best stabilization for the SnO2 was provided using the acetyl acetone (AcAc) medium. Figure 2 shows the sedimentation test for the SnO2 particles in both the iodine added and iodine-free AcAc suspension. As shown in Figure 3, the stability of the AcAc based SnO2 suspension was improved with the iodine addition. The zeta potential value plays a vital role in determining the surface charge of the particles introduced by the zeta potential. Figure 3 shows that zeta potential graph of SnO2 particles in AcAc based suspension changes from negative to zero up to 0.42 g/L iodine concentration. After this point, it increases zero to positive by changing the amount of iodine. The zeta potential has maximum value (nearly 35 mV) for 0.7 gr/L iodine concentration. Both zeta potential and sedimentation experiments show that stabilization and well-dispersed suspension are achieved by iodine addition. Iodine is used to positively charge the ceramic particles. As given reaction, protons are formed: (1)
C
H
3
C
O
C
H
2
C
O
C
H
3
+
2
I
2
⟷
I
C
H
2
C
O
C
H
2
C
O
C
H
2
I
+
2
I
-
+
2
H
+The iodine reaction between an organic solvent and its alkyls groups creates some ions which is the cause of increasing the suspension conductivity. Therefore, conductivity of acetyl acetone based suspension is much larger than other solvents. This larger conductivity with increasing iodine causes the increase of the zeta potential of ceramic suspension [35, 36].Table 1
Zeta potential and conductivity of suspensions in three solvent media.
Suspension media
Zeta potential (mV)
Conductivity (μS/cm)
Ethanol
−5.6
0.117
Acetyl acetone
+29
0.00149
Isopropyl alcohol
+55
0.0009Figure 2
Sedimentation test of SnO2 nanoparticles in iodine added AcAc and AcAc mediums: iodine added AcAc suspension at the beginning of sedimentation test (a), iodine added AcAc suspension after 24 hours (b), suspension without iodine beginning (c), and suspension without iodine after 24 hours (d).
(a)
(b)
(c)
(d)Figure 3
Zeta potential of SnO2 nanopowder in iodine added acetyl acetone medium.The evaporation of the iodine from coating layer is a rapid process, but there are still some doubts that it is purified completely. It can cause undesirable reaction and impurity during sensor application. It may act as a contaminant; hence sensor sensitivity or accuracy can change unexpectedly. For this reason, the optimization of the suspension in the absence of iodine is necessary. Because of the probable iodine effect, another suspension was prepared without iodine. The process of the suspension focused on ultrasonic dispersion in this stage. The optimization of the ultrasonic sonification was performed at various times, and power combination was used to enhance the stabilization. The optimum values for the stabilization of the suspension were observed as 20 W and 4 min. The ultrasonic sonification power and time are significant in order to minimize the agglomeration of the particles in the suspension. Excess time and ultrasonic power cause an increase in agglomeration. However, less dispersion time and ultrasonic power combination may cause the insufficient dispersion of the agglomerates. Therefore, the dispersion of the nanosized powder, especially under 100 nm, is very difficult due to the electrostatic attractive forces between the particles [37]. Figures 4(a) and 4(b) show the particle size distribution of the SnO2 nanopowders. Figure 4(a) displays the trimodel size distribution of suspension prior to the ultrasonic homogenizations process due to agglomeration. However, Figure 4(b) presents the monomodel and the narrow particle size distribution after ultrasonic homogenization. The particle size distribution of the SnO2 in the AcAc without iodine was approximately 100 nm.Figure 4
Size distribution of SnO2 nanopowder in AcAc medium before (a) and after optimum ultrasonic homogenization (b).
(a)
(b)


## 3.2. Electrophoretic Deposition of SnO2 Nanopowder

### 3.2.1. EPD in Iodine Added AcAc Based SnO2 Suspension (Process 1)

The electrophoretic deposition was performed between 50 and 150 V using AcAcI suspensions. The electrodes’ distance and depositing time were 1 cm and 30 sec, 60 sec, 90 sec, and 120 sec, respectively. The optimum deposition voltages were 100 V and 150 V for the SnO2 accumulation on the interdigital electrodes. The coating quality was adversely affected by either increasing or decreasing the deposition voltage. When the three different deposition voltages were compared, the most homogeneous coating was obtained at 100 V. Figure 5 shows that the migration of the SnO2 nanopowder at 100 V was higher than the others and resulted in higher deposition yield on any coating surface. Both 50 V and 100 V series have better coating results when compared to 150 V. Migration control of the particles becomes more difficult at higher voltage (150 V). Therefore, suspension concentration between electrodes decreases rapidly, and this causes a decrease in deposition weight.Figure 5
EPD of SnO2 nanoparticles in AcAcI medium at various voltages (50-100-150 V) and deposition time (30-60-90-120 sec).


### 3.2.2. EPD in AcAc Based SnO2 Suspension without Iodine (Process 2)

The electrophoretic deposition of the SnO2 nanopowder in the AcAc medium was successfully achieved between 100 and 150 V for a 1 cm electrode distance and various deposition times (5 sec–60 sec). As given in Figure 6, 150 V was the optimum voltage for the SnO2 deposition when compared to 100 V. As expected, the coating yield increased with deposition time for each coating voltage.Figure 6
EPD of SnO2 nanoparticles in AcAc medium at various voltages (100-150 V) and deposition time (5-15-30-45-60 sec).When compared, the EPD of the SnO2 nanopowder in the AcAc with iodine and the surface charge of the particles in the AcAcI suspension were higher than the AcAc suspension. There was no sedimentation at 24 hours in the AcAcI suspension from the sedimentation test, but nearly 5.4% of the AcAc suspension was precipitated (Figure 2). However, the migration of the SnO2 particles in the pure AcAc suspension was higher than iodine added suspension even if it has a higher surface charge. It could be explained that the increase of ionic concentration has adverse effect on double layer. Therefore, it causes the reduction of SnO2 migration during EPD [22]. The weight of EPD coating obtained at 150 V for 30 sec is nearly 0.006 gr/cm2 (6 times higher than process 1). Therefore, process 2 is more convenient for sensor applications. Also, creating a homogeneous film coating in a short coating time was the main purpose of this study. Therefore, shorter deposition times were investigated for AcAc based suspension. Efficient deposition at 100 V and 150 V for 5 sec and 15 sec produced a homogeneous SnO2 layer.


### 3.2.3.  Sintering of Coated SnO2 Nanopowder with EPD

Porosity, homogeneity, high surface area, and small grain size are the main desired properties of the sensor for increasing the adsorption into certain gases [38]. Because of this reason, a heat treatment should be applied only for the neck formation between the particles in order to enhance the mechanical properties of the deposited layer. Therefore, the microstructure of the deposited SnO2 films is controllable by the sintering temperature. Nanosized powders possess high surface energy due to their high surface area. The surface energy is the driving force for the sintering. Therefore, nanopowders can be sintered at a low sintering temperature for a shorter sintering time. The sintering temperature range of the SnO2 commercial powder fluctuates between 1000 and 1400°C, but the nanosized powder is processed at a lower sintering temperature due to its high surface energy [39, 40]. The aim at the sintering step is to determine the neck formation temperature between the SnO2 nanopowders. The surface diffusion is the dominant sintering (mass transport) mechanism for the SnO2 within a range of 500–1000°C [39]. Figures 7(a)–7(e) give the sintering behavior of the deposited SnO2 nanopowders at various temperatures. As the given figure, no neck formation was observed below 500°C (Figures 7(a)–7(c)). The neck formation between the SnO2 nanopowders was seen at 500°C and 600°C (Figures 7(d) and 7(e)). The SEM investigations showed that the homogeneous SnO2 film layer was achieved by the EPD on the Pt coated alumina substrate. The film thickness was approximately 6 μm (Figure 7(f)).Figure 7
SEM images of unsintered SnO2 (a), sintered SnO2 at 300°C-400-500-600°C for 5 minutes (b–e), and side view of film thickness (f).
(a)
Unsintered
(b)
300°C
(c)
400°C
(d)
500°C
(e)
600°C
(f)
Side view of SnO2 film


### 3.2.4. Gas Sensing Analyses of the Deposited SnO2 Films with EPD

Gas sensitivity can be controlled by the surface area and the particle size. The driving force was the high surface area and small pores in the range of the micropore or mesopore in the film structure using the nanopowder in the gas sensing applications. The sensing mechanisms of the gas sensors explained the surface reactions of the semiconducting oxide with hazardous gases. The LPG sensing performance tested the change in the resistance of the SnO2 film in the presence of the gases. When the sensor was exposed to the toxic and explosive gases, two reactions occurred on the film surface. The first reaction was the oxygen molecules in air which were physisorbed on the surface sites. They were ionized when taking an electron from the conduction band of the semiconductor. Therefore, the resistance of the gas sensors increases. When the semiconductor oxide sensor is exposed to the reducing gases, it reacts with chemisorbed oxygen. Releasing the trapped electron back to the conduction band, it causes a decrease in the resistance of the semiconductor oxide sensor [41, 42]. As given in Figure 7, the diameter of the nanopowders was smaller than 100 nm, and their pores were below 50 nm. These investigations showed that the deposited layers can be used for LPG sensing.As well as being used as domestic, commercial, and industrial fuel, it also has an area of use in the automobile sector under the name of autogas [43, 44]. The lowest explosive limit (LEL) is the minimum gas concentration that causes combustion in the air in the presence of an ignition source. The gas leakage concentration should not exceed 20% LEL (<3000 ppm) for safety reasons. Liquefied petroleum gas (LPG) was used for gas sensing experiments. The EPD deposited SnO2 sensors were placed in a cylindrical chamber (≈3 liter). The test chamber was designed to allow the circulation of the air and gas. The gas sensing measurement was performed between 250°C and 450°C for various LEL concentrations. The sensitivity of the SnO2 films was determined as S
=
R
a
/
R
g, where R
a was the resistance of the sensor in the presence of air and R
g was the resistance in the presence of the LPG [41, 45]. The resistance measurements were analyzed with the KEITHLEY 2410-C multimeter.Figures8(a) and 8(b) present the sensing results of the SnO2 sensors. Figure 8(a) shows the sensitivity variation of the SnO2 sensor as a function of the LPG concentration in the range of 10–100 LEL at different operational temperatures, namely, 300, 350, 400, and 450°C. It was observed that the sensitivity of the sensor increases along with the increasing operation temperature for all the LPG gas concentrations. These results follow a similar trend to Majumder et. al’s study, which was related to SnO2/Pd composite films deposited on the Si/SiO2 substrates with sputtering [46]. The best sensor sensitivity was observed at 450°C for all the LPG concentration. Moreover, the sensor sensitivity to the 20 and 30 LEL LPG sharply increases above the 350°C operation temperature (Figure 8(b)). It could be related to the presence of more stable adsorbed oxygen depending on the heat treatment after the coating.Figure 8
Sensitivity of fabricated SnO2 sensor with EPD: (a) for various LPG concentrations at various operating temperatures and (b) sensitivity to 20 and 30 LEL LPG at various operating temperatures.
(a)
(b)In our previous studies we have reported that the sensitivity of electrospray deposited (ESD) sensors was between 1.1 and 2.51 for 20 LEL LPG concentration [2]. The sensitivity of sensors produced by EPD at same LPG concentration was between 12 and 30. As a result, the sensitivity of EPD coated SnO2 sensors was nearly twelve times greater than ESD coated SnO2 sensors due to their highly porous structure and larger quantity of powder accumulation. According to our approach, more porous and thicker films can be produced by high deposition voltage, short deposition period, and short distance between electrodes. These were led to increase in the interaction of the particles during migration when the electric field was applied. In this case, individual particles were tended to agglomerate during EPD. These agglomerated particles were created by looser packing and thicker and more porous coating. Consequently, EPD fabricated SnO2 sensors had higher sensitivity than ESD fabricated sensors.


## 3.2.1. EPD in Iodine Added AcAc Based SnO2 Suspension (Process 1)

The electrophoretic deposition was performed between 50 and 150 V using AcAcI suspensions. The electrodes’ distance and depositing time were 1 cm and 30 sec, 60 sec, 90 sec, and 120 sec, respectively. The optimum deposition voltages were 100 V and 150 V for the SnO2 accumulation on the interdigital electrodes. The coating quality was adversely affected by either increasing or decreasing the deposition voltage. When the three different deposition voltages were compared, the most homogeneous coating was obtained at 100 V. Figure 5 shows that the migration of the SnO2 nanopowder at 100 V was higher than the others and resulted in higher deposition yield on any coating surface. Both 50 V and 100 V series have better coating results when compared to 150 V. Migration control of the particles becomes more difficult at higher voltage (150 V). Therefore, suspension concentration between electrodes decreases rapidly, and this causes a decrease in deposition weight.Figure 5
EPD of SnO2 nanoparticles in AcAcI medium at various voltages (50-100-150 V) and deposition time (30-60-90-120 sec).


## 3.2.2. EPD in AcAc Based SnO2 Suspension without Iodine (Process 2)

The electrophoretic deposition of the SnO2 nanopowder in the AcAc medium was successfully achieved between 100 and 150 V for a 1 cm electrode distance and various deposition times (5 sec–60 sec). As given in Figure 6, 150 V was the optimum voltage for the SnO2 deposition when compared to 100 V. As expected, the coating yield increased with deposition time for each coating voltage.Figure 6
EPD of SnO2 nanoparticles in AcAc medium at various voltages (100-150 V) and deposition time (5-15-30-45-60 sec).When compared, the EPD of the SnO2 nanopowder in the AcAc with iodine and the surface charge of the particles in the AcAcI suspension were higher than the AcAc suspension. There was no sedimentation at 24 hours in the AcAcI suspension from the sedimentation test, but nearly 5.4% of the AcAc suspension was precipitated (Figure 2). However, the migration of the SnO2 particles in the pure AcAc suspension was higher than iodine added suspension even if it has a higher surface charge. It could be explained that the increase of ionic concentration has adverse effect on double layer. Therefore, it causes the reduction of SnO2 migration during EPD [22]. The weight of EPD coating obtained at 150 V for 30 sec is nearly 0.006 gr/cm2 (6 times higher than process 1). Therefore, process 2 is more convenient for sensor applications. Also, creating a homogeneous film coating in a short coating time was the main purpose of this study. Therefore, shorter deposition times were investigated for AcAc based suspension. Efficient deposition at 100 V and 150 V for 5 sec and 15 sec produced a homogeneous SnO2 layer.


## 3.2.3.  Sintering of Coated SnO2 Nanopowder with EPD

Porosity, homogeneity, high surface area, and small grain size are the main desired properties of the sensor for increasing the adsorption into certain gases [38]. Because of this reason, a heat treatment should be applied only for the neck formation between the particles in order to enhance the mechanical properties of the deposited layer. Therefore, the microstructure of the deposited SnO2 films is controllable by the sintering temperature. Nanosized powders possess high surface energy due to their high surface area. The surface energy is the driving force for the sintering. Therefore, nanopowders can be sintered at a low sintering temperature for a shorter sintering time. The sintering temperature range of the SnO2 commercial powder fluctuates between 1000 and 1400°C, but the nanosized powder is processed at a lower sintering temperature due to its high surface energy [39, 40]. The aim at the sintering step is to determine the neck formation temperature between the SnO2 nanopowders. The surface diffusion is the dominant sintering (mass transport) mechanism for the SnO2 within a range of 500–1000°C [39]. Figures 7(a)–7(e) give the sintering behavior of the deposited SnO2 nanopowders at various temperatures. As the given figure, no neck formation was observed below 500°C (Figures 7(a)–7(c)). The neck formation between the SnO2 nanopowders was seen at 500°C and 600°C (Figures 7(d) and 7(e)). The SEM investigations showed that the homogeneous SnO2 film layer was achieved by the EPD on the Pt coated alumina substrate. The film thickness was approximately 6 μm (Figure 7(f)).Figure 7
SEM images of unsintered SnO2 (a), sintered SnO2 at 300°C-400-500-600°C for 5 minutes (b–e), and side view of film thickness (f).
(a)
Unsintered
(b)
300°C
(c)
400°C
(d)
500°C
(e)
600°C
(f)
Side view of SnO2 film


## 3.2.4. Gas Sensing Analyses of the Deposited SnO2 Films with EPD

Gas sensitivity can be controlled by the surface area and the particle size. The driving force was the high surface area and small pores in the range of the micropore or mesopore in the film structure using the nanopowder in the gas sensing applications. The sensing mechanisms of the gas sensors explained the surface reactions of the semiconducting oxide with hazardous gases. The LPG sensing performance tested the change in the resistance of the SnO2 film in the presence of the gases. When the sensor was exposed to the toxic and explosive gases, two reactions occurred on the film surface. The first reaction was the oxygen molecules in air which were physisorbed on the surface sites. They were ionized when taking an electron from the conduction band of the semiconductor. Therefore, the resistance of the gas sensors increases. When the semiconductor oxide sensor is exposed to the reducing gases, it reacts with chemisorbed oxygen. Releasing the trapped electron back to the conduction band, it causes a decrease in the resistance of the semiconductor oxide sensor [41, 42]. As given in Figure 7, the diameter of the nanopowders was smaller than 100 nm, and their pores were below 50 nm. These investigations showed that the deposited layers can be used for LPG sensing.As well as being used as domestic, commercial, and industrial fuel, it also has an area of use in the automobile sector under the name of autogas [43, 44]. The lowest explosive limit (LEL) is the minimum gas concentration that causes combustion in the air in the presence of an ignition source. The gas leakage concentration should not exceed 20% LEL (<3000 ppm) for safety reasons. Liquefied petroleum gas (LPG) was used for gas sensing experiments. The EPD deposited SnO2 sensors were placed in a cylindrical chamber (≈3 liter). The test chamber was designed to allow the circulation of the air and gas. The gas sensing measurement was performed between 250°C and 450°C for various LEL concentrations. The sensitivity of the SnO2 films was determined as S
=
R
a
/
R
g, where R
a was the resistance of the sensor in the presence of air and R
g was the resistance in the presence of the LPG [41, 45]. The resistance measurements were analyzed with the KEITHLEY 2410-C multimeter.Figures8(a) and 8(b) present the sensing results of the SnO2 sensors. Figure 8(a) shows the sensitivity variation of the SnO2 sensor as a function of the LPG concentration in the range of 10–100 LEL at different operational temperatures, namely, 300, 350, 400, and 450°C. It was observed that the sensitivity of the sensor increases along with the increasing operation temperature for all the LPG gas concentrations. These results follow a similar trend to Majumder et. al’s study, which was related to SnO2/Pd composite films deposited on the Si/SiO2 substrates with sputtering [46]. The best sensor sensitivity was observed at 450°C for all the LPG concentration. Moreover, the sensor sensitivity to the 20 and 30 LEL LPG sharply increases above the 350°C operation temperature (Figure 8(b)). It could be related to the presence of more stable adsorbed oxygen depending on the heat treatment after the coating.Figure 8
Sensitivity of fabricated SnO2 sensor with EPD: (a) for various LPG concentrations at various operating temperatures and (b) sensitivity to 20 and 30 LEL LPG at various operating temperatures.
(a)
(b)In our previous studies we have reported that the sensitivity of electrospray deposited (ESD) sensors was between 1.1 and 2.51 for 20 LEL LPG concentration [2]. The sensitivity of sensors produced by EPD at same LPG concentration was between 12 and 30. As a result, the sensitivity of EPD coated SnO2 sensors was nearly twelve times greater than ESD coated SnO2 sensors due to their highly porous structure and larger quantity of powder accumulation. According to our approach, more porous and thicker films can be produced by high deposition voltage, short deposition period, and short distance between electrodes. These were led to increase in the interaction of the particles during migration when the electric field was applied. In this case, individual particles were tended to agglomerate during EPD. These agglomerated particles were created by looser packing and thicker and more porous coating. Consequently, EPD fabricated SnO2 sensors had higher sensitivity than ESD fabricated sensors.


## 4. Conclusion

In this study, SnO2 nanoparticles were effectively deposited into the EPD on Pt coated alumina layer and interdigital electrode. The optimum stabilization of the SnO2 nanopowder was obtained by dispersing the powders into the acetylacetone medium. The effect of the iodine on the dispersion and deposition of the SnO2 powders was evaluated. The effective SnO2 deposition was performed at 100 V and 150 V for 5 sec and 15 sec in the iodine-free AcAc based suspension when the compared iodine was added to the AcAc solution. The sintering of the coating was examined at different temperatures within the range of 300–600°C. The optimum neck formation was achieved at 500°C for 5 min. The coated film thickness was nearly 6 μm. The gas sensing experiments on the LPG were performed for various LPG LEL concentrations. The fabricated sensor with the EPD showed good sensitivity to the 20 LEL LPG at 450°C operating temperature. The best sensitivity of the deposited sensors with EPD at 450°C to 20 LEL LPG was measured at 30.



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*Source: 971473-2015-05-27.xml*