# Combustion Synthesis of Fe-Incorporated SnO2 Nanoparticles Using Organometallic Precursor Combination

Authors: Thomas K. Barkley; Jenna E. Vastano; James R. Applegate; Smitesh D. Bakrania
Journal: Advances in Materials Science and Engineering
 (2012)

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## Abstract

Synthesis of nanomaterials within flames has been demonstrated as a highly scalable and versatile approach for obtaining a variety of nanoparticles with respect to their chemistry, composition, size, morphology, and dimensionality. Its applicability can be amplified by exploring new material systems and providing further control over the particle characteristics. This study focused on iron-incorporated SnO2 nanoparticles generated using an inverse coflow diffusion flame burner that supported a near-stoichiometric methane-air combustion. A liquid organometallic precursor solution of Sn(CH3)4 and Fe(CO)5 was used to produce 11–14 nm nanocrystalline particles. Synthesized particles were analyzed using TEM, XRD, and XEDS to characterize for size and composition. A flame temperature field was obtained to map particle evolution within the flame. A range of conditions and parameters were studied to specifically generate targeted particles. The study augments related research towards increasing the production potential of combustion synthesis.


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## Body

## 1. Introduction

Nanoparticles are becoming increasingly valuable for applications in a wide range of engineering systems. In addition to uses in many electrical and catalytic applications, nanoparticles such as tin dioxide (SnO2) show great potential as sensing agents in solid-state gas detectors [1, 2]. High aspect ratio SnO2 particles have been demonstrated to improve sensitivity and selectivity of toxic gas detectors [3, 4]. Performance of these particles is highly dependent on morphology, composition, and size [5–9]. For instance, iron-doped SnO2 nanoparticles have been shown as strong candidates for potent gas sensing materials with improved selectivity towards methane, butane, and H2S [10, 11]. At the same time, these nanoparticles are being actively researched for their diluted magnetic semiconductor (DMS) properties [12–14]. Current efforts are focused on the research of effective production methods for such nanomaterials—production methods that are facile and robust for scaleup.Various chemical and physical synthesis methods have been employed to generate composite or iron-doped SnO2 materials, including coprecipitation [10, 14], mechanical alloying [12], cosputtering [1, 6], sol-gel method [13], and others [11, 15]. However, the need for vacuum conditions or solvents is a considerable hurdle for potential scaleup. Combustions synthesis, on the other hand, offers many advantages over these methods [16–21]. The process is self-purifying, continuous, and affords appreciably high production rates. Current commercial production rates approach several million metric tons/year [16, 17, 22]. Additionally, one-dimensional iron-doped SnO2 structures [23] and thin films [2] have already been successfully produced using combustion synthesis approaches. These approaches, however, use chloride-based precursors that can potentially poison the product materials depending on the application [24, 25] or require absorption of the hydrochloric acid as a byproduct [23]. Though SnO2 and F2O3 nanoparticles have been generated from organometallic precursors individually, a combined combustion synthesis from these precursors has yet to be investigated. As a result, there is a need to explore other compatible precursors for synthesis of iron-doped SnO2 nanoparticles, specifically structures other than commonly found composite nanoarchitectures.This paper describes a new method to produce iron-incorporated SnO2 which uses a combination of organometallic precursors in a one-step solvent-free combustion synthesis technique. A bench-top coflow diffusion flame burner was designed for combustion synthesis and sampling of nanoparticles. The facility was configured to deliver a premixed iron pentacarbonyl (IPC) and tetramethyl tin (TMT) precursor solution to an inverse diffusion flame. Based on the particle size, morphology, and chemical composition of the product powders, a model of particle formation is suggested that relies on the effects of flame environment on precursor decomposition and the unique compositional features of the nanoparticles. Therefore, the current work adds to the vast library of nanomaterials that are feasible via combustion synthesis.


## 2. Experimental Procedure

The facility was designed to provide a compact experimental apparatus with a highly configurable flame environment. The facility exhibited concentric steel tubes to support a flame with four chambers corresponding to the flow of fuel, oxidizer, precursor carrier gas, and the exterior shroud gas. The combustion-synthesized particles were collected on a water-cooled bulk sampling plate. Transmission Electron Microscope (TEM) sampling was performed via pneumatic piston-cylinder actuator. For these experiments, the nanopowders were synthesized using a methane-air inverse diffusion flame. Argon was used as a carrier gas to deliver the liquid-phase precursor solution to the high-temperature reaction zone.


### 2.1. Experimental Facility

Figure1 presents a schematic of the custom-built facility for combustion synthesis. The inner diameter of the tube supplying the fuel was 7.6 mm, while the inner diameter of the precursor delivery tube at the burner exit was 1.7 mm. Omega FLD Series rotameters were used to monitor flow rates of the reaction gases. Methane (CH4, 99.99%, Praxair) flow rate was maintained at 180 mL/min and argon carrier gas (Ar, 99.998%, GTS-Welco) flow rate at 50 mL/min. Depending on the precursor selection, compressed air (99.8%, GTS-Welco) flow rates ranged from 1800 to 2300 mL/min. Gases were configured to yield an inverse diffusion flame at the co-flow burner exit. No shroud gas was used for these experiments. A steel tube chimney with dimensions 108 mm diameter and 254 mm height was used to improve collection efficiency of the products. The precursor reservoir with 21 mL capacity and 6.35 mm diameter glass beads was used to deliver vapor-phase precursors simultaneously to the synthesis region by bubbling argon through the precursor solution.Figure 1
A custom-built bench-top coflow diffusion burner with premixed precursor delivery bubbler unit. Piston-cylinder actuator for TEM sampling and water-cooled bulk sampling plate for nanopowder collection.The synthesis products were collected in two ways. TEM samples were collected using a compressed air piston-cylinder actuator with a mounted 3 mm grid (300 mesh copper grid with carbon film). Typical residence time for the collection in the flame was 2 ms, measured using a high-speed imaging camera. Bulk samples were thermophoretically collected on microscope glass slides mounted on an aluminum block that was maintained at a nominal temperature of 22°C. The bulk sampling plate was typically located at 120 mm above the surface of the burner with a maximum collection time of 10 mins. The flame region was characterized for average temperature at multiple locations along the vertical axis of the burner using S-type thermocouple with a bead diameter of 10μm. The thermocouple was threaded through an alumina sheathing for temperature measurements, and the temperature readings were corrected to account for radiative heat loss.


### 2.2. Chemistry

Synthesis of nanopowders was carried out by combusting a solution of liquid-phase iron pentacarbonyl (IPC, Fe(CO)5, >99.99% trace metals basis, Sigma Aldrich) and tetramethyl tin (TMT, Sn(CH3)4, 95% purity, Sigma Aldrich) precursors. Table 1 lists the relevant thermophysical properties of these chemicals as obtained from the supplier. Of interest are the boiling points, flash points, and phase of the precursors. These properties were comparable for the precursors considering the steep temperature gradients in the flame which ensured the compatibility of these precursors for the current premixed delivery system. In the delivery system, the solution was contained in a bubbler reservoir, where glass beads were included to facilitate evaporation of the liquid mixture. Argon gas was bubbled through the reservoir at room temperature. Low boiling points of the precursors yielded nearly saturated argon gas flow. An entrained precursor solution of 2.5 at % IPC in TMT was targeted for delivery to the burner exit.Table 1
Relevant thermophysical properties of tetramethyl tin (TMT) and iron pentacarbonyl (IPC) with respect to the combustion synthesis environment.
PropertySn(CH3)4Fe(CO)5Melting point−54°C−20°CBoiling point75°C103°CFlash point−12°C−15°CPhaseLiquidLiquidUsing global reactions for the stoichiometric combustion of CH4, TMT, and IPC fuels, experiments were conducted to yield near-stoichiometric combustion of all the fuels (or precursors). Therefore, the air flow rate was adjusted for complete oxidation of precursors while keeping the CH4 flow rate constant.


### 2.3. Material Characterization

The solid-phase combustion products were characterized for size, morphology, and chemical composition using a variety of methods. Scanning electron microscopy (SEM, LEO 1530) was used for bulk material morphology, while TEM imaging (Hitachi H-600AB) was performed for detailed size and morphology analysis. Particle size distributions were obtained using a semiautomated MATLAB-based approach described in Bakrania et al. [26] for particle counts exceeding 100. X-ray diffraction (XRD) analysis on the powders was performed using Scintag LT-801 with Cu-Kα X-ray source. Average crystallite size was estimated using Scherrer crystallite size analysis. X-ray energy dispersive spectroscopy (XEDS) was performed on samples in conjunction with the SEM imaging, while inductively coupled plasma (ICP) analysis was performed to study the elemental composition of the products.


## 2.1. Experimental Facility

Figure1 presents a schematic of the custom-built facility for combustion synthesis. The inner diameter of the tube supplying the fuel was 7.6 mm, while the inner diameter of the precursor delivery tube at the burner exit was 1.7 mm. Omega FLD Series rotameters were used to monitor flow rates of the reaction gases. Methane (CH4, 99.99%, Praxair) flow rate was maintained at 180 mL/min and argon carrier gas (Ar, 99.998%, GTS-Welco) flow rate at 50 mL/min. Depending on the precursor selection, compressed air (99.8%, GTS-Welco) flow rates ranged from 1800 to 2300 mL/min. Gases were configured to yield an inverse diffusion flame at the co-flow burner exit. No shroud gas was used for these experiments. A steel tube chimney with dimensions 108 mm diameter and 254 mm height was used to improve collection efficiency of the products. The precursor reservoir with 21 mL capacity and 6.35 mm diameter glass beads was used to deliver vapor-phase precursors simultaneously to the synthesis region by bubbling argon through the precursor solution.Figure 1
A custom-built bench-top coflow diffusion burner with premixed precursor delivery bubbler unit. Piston-cylinder actuator for TEM sampling and water-cooled bulk sampling plate for nanopowder collection.The synthesis products were collected in two ways. TEM samples were collected using a compressed air piston-cylinder actuator with a mounted 3 mm grid (300 mesh copper grid with carbon film). Typical residence time for the collection in the flame was 2 ms, measured using a high-speed imaging camera. Bulk samples were thermophoretically collected on microscope glass slides mounted on an aluminum block that was maintained at a nominal temperature of 22°C. The bulk sampling plate was typically located at 120 mm above the surface of the burner with a maximum collection time of 10 mins. The flame region was characterized for average temperature at multiple locations along the vertical axis of the burner using S-type thermocouple with a bead diameter of 10μm. The thermocouple was threaded through an alumina sheathing for temperature measurements, and the temperature readings were corrected to account for radiative heat loss.


## 2.2. Chemistry

Synthesis of nanopowders was carried out by combusting a solution of liquid-phase iron pentacarbonyl (IPC, Fe(CO)5, >99.99% trace metals basis, Sigma Aldrich) and tetramethyl tin (TMT, Sn(CH3)4, 95% purity, Sigma Aldrich) precursors. Table 1 lists the relevant thermophysical properties of these chemicals as obtained from the supplier. Of interest are the boiling points, flash points, and phase of the precursors. These properties were comparable for the precursors considering the steep temperature gradients in the flame which ensured the compatibility of these precursors for the current premixed delivery system. In the delivery system, the solution was contained in a bubbler reservoir, where glass beads were included to facilitate evaporation of the liquid mixture. Argon gas was bubbled through the reservoir at room temperature. Low boiling points of the precursors yielded nearly saturated argon gas flow. An entrained precursor solution of 2.5 at % IPC in TMT was targeted for delivery to the burner exit.Table 1
Relevant thermophysical properties of tetramethyl tin (TMT) and iron pentacarbonyl (IPC) with respect to the combustion synthesis environment.
PropertySn(CH3)4Fe(CO)5Melting point−54°C−20°CBoiling point75°C103°CFlash point−12°C−15°CPhaseLiquidLiquidUsing global reactions for the stoichiometric combustion of CH4, TMT, and IPC fuels, experiments were conducted to yield near-stoichiometric combustion of all the fuels (or precursors). Therefore, the air flow rate was adjusted for complete oxidation of precursors while keeping the CH4 flow rate constant.


## 2.3. Material Characterization

The solid-phase combustion products were characterized for size, morphology, and chemical composition using a variety of methods. Scanning electron microscopy (SEM, LEO 1530) was used for bulk material morphology, while TEM imaging (Hitachi H-600AB) was performed for detailed size and morphology analysis. Particle size distributions were obtained using a semiautomated MATLAB-based approach described in Bakrania et al. [26] for particle counts exceeding 100. X-ray diffraction (XRD) analysis on the powders was performed using Scintag LT-801 with Cu-Kα X-ray source. Average crystallite size was estimated using Scherrer crystallite size analysis. X-ray energy dispersive spectroscopy (XEDS) was performed on samples in conjunction with the SEM imaging, while inductively coupled plasma (ICP) analysis was performed to study the elemental composition of the products.


## 3. Results

### 3.1. Combustion Environment

The co-flow methane-air inverse diffusion flame at the specified flow rates resulted in a blue flame approximately 65 mm in height without the precursor solution present. As the precursor solution was introduced through the central precursor tube, a yellow luminous flame resulted indicating particle formation (see Figure2). To ensure both precursors were delivered to the flame region, individual precursors (pure TMT and pure IPC) were tested separately. The pure precursors yielded the distinct luminous flames to produce respective iron oxide and tin dioxide as demonstrated by several other studies [21, 22, 26–31]. To introduce catalytic quantities of iron in the product powders, 2.5 atc% IPC was added to TMT in the bubbler and sealed. The introduction of this precursor solution produced a distinctly luminous flame compared to the pure TMT system.Images of the inverted diffusion flame (a) without precursors and (b) with a mixture of 2.5 at% IPC in TMT present. As a reference, the external diameter of the burner is 20.3 mm.
(a)(b)Flame temperatures were measured along the height of the flame at the central axis to characterize the reaction zone using a thermocouple mounted to the sampling stand. Temperatures were measured for three different systems for comparison: methane-air flame without precursor solution, pure TMT as the precursor, and a solution of 2.5 at% IPC in TMT. Figure3 presents the temperature profile with a rapid increase in temperature from just above the burner surface to a gradual drop in temperature at higher locations for all three systems. The peak temperature was observed at approximately 23 mm above the burner for all three systems. The flame without any precursor exhibited a peak temperature of ~1100°C, while the flame with pure TMT observed a drop in peak temperature to ~900°C that can be attributed to the cooling from the additional vapor-phase precursor solution. The high peak temperature of ~1300°C for the IPC-TMT system can be explained by the highly exothermic decomposition of precursors which, as a result, yields relatively higher temperatures in the product gases as well. The temperatures were corrected for radiation, and the relative uncertainty for the measured temperatures was estimated at 5%. Any inadvertent material deposits on the thermocouple were cleared for accurate assessment of flame temperatures.Figure 3
Radiation-corrected thermocouple temperature measurements above the central axis of the burner. Plot includes temperature profiles for the reaction zone without precursors, with pure TMT, and with 2.5 at% IPC-TMT precursor solution.


### 3.2. Material Characterization

The combustion-synthesized powders were collected on microscope slides at a rate of 3–5 mg/min. Grayish-white fine powders were obtained with the IPC-TMT precursor solution at a height of 117 mm on the water-cooled sampling plate. The tubular steel chimney was only used for XRD sampling runs. Figure4 presents an XRD spectra of the 2.5 at% IPC-TMT precursor solution product as obtained from the experiments. All the peaks were identified for the cassiterite phase of SnO2 (JCPDS Ref. No. 41–1445), while no peaks were attributed to any iron or iron-based compounds. Scherrer crystallite size analysis performed on the 110 peak of SnO2 yielded average crystallite size of 16.4 nm for the SnO2 particles.Figure 4
X-ray diffraction spectra of 2.5 at% IPC-TMT precursor solution products. Peaks identified as cassiterite phase SnO2. No peaks were attributed to the presence of any iron or iron-based compounds.Figures5(a) and 5(b) provide SEM images of the bulk samples demonstrating granular structure at lower magnification while a porous architecture is identified for the individual grains, respectively. XEDS analysis conducted on the SEM samples confirmed the presence of tin (Sn) and oxygen (O), at the same time indicating presence of elemental iron (Fe) at 3.3 wt% (6.8 at%). The presence of elemental iron was also confirmed using inductively couple plasma (ICP) analysis yielding atomic ratio of 0.069 for Fe : Sn (2.2 at% Fe in SnO2 assuming stoichiometric oxygen content for tin), which corroborates well with initial precursor concentration. Figures 5(c) and 5(d) are TEM images of grid samples collected using the actuated piston cylinder at a height of 46 mm. These samples show typically spherical primary nanoparticles forming agglomerated nanostructures.SEM and TEM images of nanoparticle products from the combustion synthesis. The majority of the powders were identified as tin dioxide using XEDS analysis.
(a)(b)(c)(d)TEM images were used to determine the particle size distribution of the primary particles using a semiautomated image analysis. Figure6 provides a primary particle size distribution obtained for multiple TEM images originating from a single sampling at 64 mm height above the burner. As seen, the geometric mean of 11.4 nm was calculated for the precursor solution samples with over 150 particles counted. A subsequent study on how the average primary particle size varies above the height of the burner at three locations (25 mm, 33 mm, and 41 mm) yielded average primary particle sizes of 6.8 nm, 8.7 nm, and 14.3 nm above the burner surface, respectively, demonstrating an appreciable growth as the particles move across the peak flame temperatures at ~23 mm above the burner surface. The calculated average primary particle sizes (11–14 nm) correspond well with the XRD crystallite sizes analyzed (16 nm) using Scherrer analysis considering differences in the two approaches—suggesting majority of the primary particles exist as single crystals.Figure 6
Particle size analysis of TEM samples. Particle size distribution obtained using a semiautomated sizing approach. Average size at height of 64 mm above the burner was11.4±1.2 nm.


### 3.3. Investigating Iron

Considering no iron compounds were identified using XRD other than the elemental presence detected using ICP and XEDS, two possibilities exist for the ultimate fate of Fe presence in SnO2 nanoparticles: (a) the iron compounds (most probably oxides) are at low enough concentrations in the products that they cannot be distinctly identified with XRD or (b) the iron is incorporated into the SnO2 lattice, generating iron-doped tin dioxide nanopowders. To investigate the first hypothesis, an increased concentration of 10 at% IPC in TMT was tested to produce a higher iron-based component within tin dioxide nanopowders to assist XRD identification. Subsequent XRD analyses of the products from 10 at% IPC yielded identical results when compared to the 2.5 at% IPC—only cassiterite-phase tin dioxide was identified while no peaks could be attributed to any iron or iron based compound. These results are in agreement with the recently published work by Alexandrescu and co-workers [32] using IPC and TMT as precursors with laser pyrolysis, where no iron compounds were identified. Melghit and Bouziane [15] also demonstrated the absence of iron-based compounds in tin dioxide powders and attributed the outcome to Fe atoms substituting Sn in the lattice with comparable iron concentrations to this study. Additionally, the nanopowders with higher iron-content, when analyzed with TEM image analysis, produced a mean primary particle size of 13 nm with over 500 particles counted (sampled at 64 mm height). XRD analysis yielded crystallite diameter of 14.5 nm for these samples. Therefore, no appreciable change in primary particle size was observed with increased IPC concentration.


## 3.1. Combustion Environment

The co-flow methane-air inverse diffusion flame at the specified flow rates resulted in a blue flame approximately 65 mm in height without the precursor solution present. As the precursor solution was introduced through the central precursor tube, a yellow luminous flame resulted indicating particle formation (see Figure2). To ensure both precursors were delivered to the flame region, individual precursors (pure TMT and pure IPC) were tested separately. The pure precursors yielded the distinct luminous flames to produce respective iron oxide and tin dioxide as demonstrated by several other studies [21, 22, 26–31]. To introduce catalytic quantities of iron in the product powders, 2.5 atc% IPC was added to TMT in the bubbler and sealed. The introduction of this precursor solution produced a distinctly luminous flame compared to the pure TMT system.Images of the inverted diffusion flame (a) without precursors and (b) with a mixture of 2.5 at% IPC in TMT present. As a reference, the external diameter of the burner is 20.3 mm.
(a)(b)Flame temperatures were measured along the height of the flame at the central axis to characterize the reaction zone using a thermocouple mounted to the sampling stand. Temperatures were measured for three different systems for comparison: methane-air flame without precursor solution, pure TMT as the precursor, and a solution of 2.5 at% IPC in TMT. Figure3 presents the temperature profile with a rapid increase in temperature from just above the burner surface to a gradual drop in temperature at higher locations for all three systems. The peak temperature was observed at approximately 23 mm above the burner for all three systems. The flame without any precursor exhibited a peak temperature of ~1100°C, while the flame with pure TMT observed a drop in peak temperature to ~900°C that can be attributed to the cooling from the additional vapor-phase precursor solution. The high peak temperature of ~1300°C for the IPC-TMT system can be explained by the highly exothermic decomposition of precursors which, as a result, yields relatively higher temperatures in the product gases as well. The temperatures were corrected for radiation, and the relative uncertainty for the measured temperatures was estimated at 5%. Any inadvertent material deposits on the thermocouple were cleared for accurate assessment of flame temperatures.Figure 3
Radiation-corrected thermocouple temperature measurements above the central axis of the burner. Plot includes temperature profiles for the reaction zone without precursors, with pure TMT, and with 2.5 at% IPC-TMT precursor solution.


## 3.2. Material Characterization

The combustion-synthesized powders were collected on microscope slides at a rate of 3–5 mg/min. Grayish-white fine powders were obtained with the IPC-TMT precursor solution at a height of 117 mm on the water-cooled sampling plate. The tubular steel chimney was only used for XRD sampling runs. Figure4 presents an XRD spectra of the 2.5 at% IPC-TMT precursor solution product as obtained from the experiments. All the peaks were identified for the cassiterite phase of SnO2 (JCPDS Ref. No. 41–1445), while no peaks were attributed to any iron or iron-based compounds. Scherrer crystallite size analysis performed on the 110 peak of SnO2 yielded average crystallite size of 16.4 nm for the SnO2 particles.Figure 4
X-ray diffraction spectra of 2.5 at% IPC-TMT precursor solution products. Peaks identified as cassiterite phase SnO2. No peaks were attributed to the presence of any iron or iron-based compounds.Figures5(a) and 5(b) provide SEM images of the bulk samples demonstrating granular structure at lower magnification while a porous architecture is identified for the individual grains, respectively. XEDS analysis conducted on the SEM samples confirmed the presence of tin (Sn) and oxygen (O), at the same time indicating presence of elemental iron (Fe) at 3.3 wt% (6.8 at%). The presence of elemental iron was also confirmed using inductively couple plasma (ICP) analysis yielding atomic ratio of 0.069 for Fe : Sn (2.2 at% Fe in SnO2 assuming stoichiometric oxygen content for tin), which corroborates well with initial precursor concentration. Figures 5(c) and 5(d) are TEM images of grid samples collected using the actuated piston cylinder at a height of 46 mm. These samples show typically spherical primary nanoparticles forming agglomerated nanostructures.SEM and TEM images of nanoparticle products from the combustion synthesis. The majority of the powders were identified as tin dioxide using XEDS analysis.
(a)(b)(c)(d)TEM images were used to determine the particle size distribution of the primary particles using a semiautomated image analysis. Figure6 provides a primary particle size distribution obtained for multiple TEM images originating from a single sampling at 64 mm height above the burner. As seen, the geometric mean of 11.4 nm was calculated for the precursor solution samples with over 150 particles counted. A subsequent study on how the average primary particle size varies above the height of the burner at three locations (25 mm, 33 mm, and 41 mm) yielded average primary particle sizes of 6.8 nm, 8.7 nm, and 14.3 nm above the burner surface, respectively, demonstrating an appreciable growth as the particles move across the peak flame temperatures at ~23 mm above the burner surface. The calculated average primary particle sizes (11–14 nm) correspond well with the XRD crystallite sizes analyzed (16 nm) using Scherrer analysis considering differences in the two approaches—suggesting majority of the primary particles exist as single crystals.Figure 6
Particle size analysis of TEM samples. Particle size distribution obtained using a semiautomated sizing approach. Average size at height of 64 mm above the burner was11.4±1.2 nm.


## 3.3. Investigating Iron

Considering no iron compounds were identified using XRD other than the elemental presence detected using ICP and XEDS, two possibilities exist for the ultimate fate of Fe presence in SnO2 nanoparticles: (a) the iron compounds (most probably oxides) are at low enough concentrations in the products that they cannot be distinctly identified with XRD or (b) the iron is incorporated into the SnO2 lattice, generating iron-doped tin dioxide nanopowders. To investigate the first hypothesis, an increased concentration of 10 at% IPC in TMT was tested to produce a higher iron-based component within tin dioxide nanopowders to assist XRD identification. Subsequent XRD analyses of the products from 10 at% IPC yielded identical results when compared to the 2.5 at% IPC—only cassiterite-phase tin dioxide was identified while no peaks could be attributed to any iron or iron based compound. These results are in agreement with the recently published work by Alexandrescu and co-workers [32] using IPC and TMT as precursors with laser pyrolysis, where no iron compounds were identified. Melghit and Bouziane [15] also demonstrated the absence of iron-based compounds in tin dioxide powders and attributed the outcome to Fe atoms substituting Sn in the lattice with comparable iron concentrations to this study. Additionally, the nanopowders with higher iron-content, when analyzed with TEM image analysis, produced a mean primary particle size of 13 nm with over 500 particles counted (sampled at 64 mm height). XRD analysis yielded crystallite diameter of 14.5 nm for these samples. Therefore, no appreciable change in primary particle size was observed with increased IPC concentration.


## 4. Discussion

The literature presents several examples of precursor’s properties and chemistry influencing the resulting product materials in combustion synthesis [33–36]. Therefore, the choice of specific precursors used in this study was deliberate to ensure doped products as opposed to nanocomposites metal oxides. Figure 7 presents a schematic of how a relatively large difference in decomposition temperatures of component precursors in a solution can yield different nanoparticle architectures: composites versus doped or solid-solution systems. When the decomposition temperatures are significantly different (or involve varying phase precursors), the subsequent particle formation is decoupled between the two component systems leading to a composite system (left on Figure 7), while a relatively similar decomposition temperature and particle formation time scales can potentially lead to a doped or a solid solution system (right on Figure 7). A doped system also has to be favored by the atomic or ionic radii interactions within the specific crystal structure [1, 11]. On the other hand, higher doping levels can result in phase segregation within a solid-solution to ultimately yield a nanocomposite system that is commonly observed in alloying [37]. For the current system, it can be assumed the later scenarios dominate for the Fe-incorporated SnO2 material obtained. Vapor-phase TMT decomposition can occur at much lower temperatures than documented decomposition temperatures [38] and IPC already exhibits decomposition temperature that is as low as 200°C. Therefore, early comparable decomposition locations for the two precursors and subsequent particle formation steps can be attributed to the observed particle composition.Figure 7
Potential pathways to composite or doped nanomaterial formation as a function of temperature above the burner.More importantly, the absence of iron-based compounds from XRD analysis can be sufficiently explained by a conclusive investigation conducted by Castro and coworkers [39] on SnO2-Fe2O3 nanopowders. Their work demonstrated and confirmed surface segregation of iron phases as the concentration of iron increased within SnO2. As a result of this phenomenon, at lower concentrations of up to 30 mol % Fe, no identifiable features of iron-based compounds are present on X-ray spectra of SnO2. The eventual encapsulation of SnO2 was supported by the combination of XEDS and HRTEM analysis on the particles as a function of Fe concentration. The work by Castro et al. substantiates the observations on combustion-synthesized powders presented here and results of other similar studies [15, 32].The primary particle sizes for the combustion-synthesized Fe-incorporated SnO2 were competitive to nanoparticles obtained using other methods [2, 10, 11, 13]. With respect to the varying concentration of IPC in TMT, neither the crystallite size nor the primary particle sizes indicated any significant changes in sizes. This result is in contrast with other studies involving changing iron dopant concentration in SnO2 that have observed a decrease in particle size as concentrations of iron increases [11, 13, 32, 39]. On the other hand, a similar trend was exhibited by Liu and coworkers where the increase in dopant concentration yielded larger crystallite sizes [23]. However, the increase in size was a result of producing high aspect ratio Fe-doped SnO2 particles in Liu et al.’s study [23] whereas no one-dimensional nanoparticles were identified in the current system.Considering, this study focused on catalytic quantities of iron incorporated in SnO2 further experiments on higher concentrations of IPC in TMT are necessary. Such an investigation can potentially yield core-shell structures demonstrated by Castro et al. [39] while simultaneously establishing a clearer trend between dopant concentration and particle size and morphology.


## 5. Conclusion

The demonstration of the new route to the synthesis of iron-incorporated SnO2 in a combustion synthesis system adds to several successful production examples of metal oxides with metals in flames [23, 40–45]. Importantly, this work uses precursors that do not add impurities such as chlorides to the product materials—a feature that is well suited for continuous high-volume production of nanoparticles. The combustion-synthesized nanoparticle properties such as size and morphology are competitive with other synthesis approaches that have demonstrated iron-incorporated SnO2 particles. While the primary particle sizes are sufficiently small at 11–13 nm, further control over particle dimensions and morphology can significantly benefit their potential applications.



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*Source: 685754-2012-02-28.xml*