The laser pyrolysis is a powerful and a versatile tool for the gas-phase synthesis of nanoparticles. In this paper, some fundamental and applicative characteristics of this technique are outlined and recent results obtained in the preparation of gamma iron oxide ( ) and titania ( ) semiconductor nanostructures are illustrated. Nanosized iron oxide particles (4 to 9 nm diameter values) have been directly synthesized by the laser-induced pyrolysis of a mixture containing iron pentacarbonyl/air (as oxidizer)/ethylene (as sensitizer). Temperature-dependent Mossbauer spectroscopy shows that mainly maghemite is present in the sample obtained at higher laser power. The use of selected samples for the preparation of water-dispersed magnetic nanofluids is also discussed. nanoparticles comprising a mixture of anatase and rutile phases were synthesized via the laser pyrolysis of - (vapors) based gas-phase mixtures. High precursor concentration of the oxidizer was found to favor the prevalent anatase phase (about 90%) in the titania nanopowders.

1. Introduction

In recent years, research interests for the preparation and application of oxide semiconductor photocatalysts have continuously grown [1]. Particular attention is paid to the use of semiconductor materials as photocatalysts for the removal of organic and inorganic species from aqueous or gas phase. This method has been suggested in environmental protection due to its ability to oxidize the organic and inorganic substrates [2]. Several steps should characterize the heterogeneous photocatalysis reaction among which most important should be the adsorption and the reaction onto the surface [3].

Studies were made on compositions consisting mainly of various oxide semiconductors. For instance, commonly used Fe2O3 semiconductor oxide is known for its catalytic activity [4, 5]. TiO2 nanoparticles offer additional advantages (low cost, chemical inertness, highly photo-activity, and suitable band gap (Eg = 3.2 eV)) [68].

The photocatalytic activity of a particulate semiconductor system depends on the crystal structure, crystallinity, particle size and shape, size distribution, surface area, and surface hydroxyls. Considerable enhancement of the absorption can be observed in small nanocrystals, where the surface-to-volume ratio is very high and the share of the surface atoms is sufficiently large. Consequently, the synthesis method plays a fundamental role.

A wide variety of gas-phase techniques has been developed for the fabrication of nanoparticulate structures [9] which could allow for homogeneous nucleation and may provide to some extent the control of particle size, particle shape, size distribution, particle composition, and degree of particle agglomeration. Among these synthesis procedures, the laser pyrolysis technique has been developed recently as a powerful tool for the synthesis of technological important nanomaterials such as metallic (Fe, Ti) oxides and composites [1013], silicon crystals [14], nanocarbon [15], and iron-siloxane polymer nanoparticles [16].

This paper represents an extension of our earlier analysis on the principles of the laser pyrolysis and its applications [17]. Here, we shortly discuss the background of the method and recent development in the field, with special emphasis on the preparation of two types of semiconductor photocatalysts: maghemite iron oxide and titanium dioxide. In Section 2, the pyrolysis of Fe(CO)5-based gas mixtures and the preparation of magnetic nanofluids are presented in a sequence relevant for the phenomenology of the process and the nanopowder structure. In Section 4, main characteristics of the laser-sensitized pyrolysis of TiCl4-based mixtures for producing titania and anatase titania in connection with their specific structural characteristics are discussed.

2. Laser Pyrolysis Synthesis

2.1. Photochemical Aspects of the Laser Pyrolysis

The specific features of the CO2 laser pyrolysis rely on the IR vibrational photochemistry. The process is based on the overlapping of the emission line of the laser (the strong 10P (20) line that peaks at 10.591 μm) with an absorption line of one or more gas precursors [17]. The molecular mechanism involves the increase of the internal energy of the ground electronic state, the evolution of the vibrational states through collisional relaxation processes, and finally the thermochemical reactions. Flynn et al. [18] show that in any environment where multiple collisions occur on the time scale of a chemical reaction, the vibrational modes of a polyatomic molecule will equilibrate, and reaction occurs without energy localization in a single mode. An additional substance, the so-called sensitizer is used in case of nonabsorbing gas precursors. It will absorb the energy and transmit it to the precursors by collisions. This energy transfer agent plays a high practical role (detailed for ethylene in what follows) because it assures the coupling between the laser radiation and the absorbing system. As a final effect of the coupling between the laser radiation and the absorbing system, the laser acts as a localized heat source. As compared to heating the gases in a furnace, the laser heating is a localized one occurring only in a small volume delimitated by the radiation cross section and the emergent gas flows. Short millisecond-scale residence times, spatial uniformity of the reaction zone, and continuous source of activation energy are the key attributes of the process.

Fe(CO)5 and TiCl4 are greatly used as precursors in conventional CVD or in photolytic or thermally laser-induced processes [19]. Fe(CO)5 and TiCl4 molecules meet also other prerequisites for CVD, like stability and relevant vapor pressure at room temperature (around 25 torr and 8 torr at 300 K, resp.). The IR spectra of both of Fe(CO)5 and TiCl4 present no absorption bands near the emission frequencies of the CO2 laser.

In the sensitized CO2 laser pyrolysis of Fe(CO)5/TiCl4, the IR radiation is used to resonantly excite C2H4 sensitizer. The absorption coefficient of C2H4 at the laser radiation wavelength of the usual CO2 lasers is  torr-1 cm-1. Ethylene is excited in a superposition of two fundamentals: ν7 (949.3 cm-1) and ν8 (940.6 cm-1). The dissociation energy H2C-CH-H (for one hydrogen stripping) is rather high (103 Kcal/mol [20]).

Ideally, it is supposed that ethylene only transfers its energy by collisions to the other precursors, but do not participate in the reaction. However, the study of the evolution of the exhaust gases often shows that at higher temperatures ethylene could also decompose. Indeed, as a first product of decomposition, acetylene is released and appears as traces in the IR spectrum of the exhaust gases. One should note that the observed C2H4 dehydrogenation could be significantly promoted by the active Fe sites generated by Fe(CO)5 dissociation. As shown in [21], although the thermodynamically favored process is the iron pentacarbonyl dissociation, the hydrocarbon decomposition could be speeded up by the catalytic surface of freshly formed iron nanoparticles.

2.2. Advantages and Drawbacks

The laser pyrolysis processes are characterized by high temperatures, fast heating rates, and short reaction times. These features make the laser pyrolysis attractive method for the manufacture of technological useful materials at lower costs compared to conventional gas-phase processes (such as the flame spray processes). Some other advantages are (i) the relative simple equipment, (ii) the versatility—the formation of virtually any nanoproducts, provided a suitable choice of precursors, and (iii) formation of high purity products.

The drawbacks of the laser pyrolysis technique are sometimes found in the constraints imposed on the precursors [6]: the desired elements must be present in vapor phase and at least one reactant should contain an infrared absorption band for the coupling of the energy with the laser beam.

2.3. Experimental Set-Up

The flow reactor is the core of the laser pyrolysis technique, ensuring the practical application of the characteristic interplay between resonant and nonresonant processes. It was presented in details elsewhere [17]. A schematic view of the setup is presented in Figure 1. Briefly, the system is based on a cross-flow configuration. The reactant flow emerges in the reactor through a nozzle system where it is orthogonally intersected by the focused IR radiation beam. Pyrolysis in the gas phase occurs in the small volume defined by the radiation-gases crossing where a “flame” usually appears. It is believed that the visible emission is mainly resulting from the hot freshly nucleated particles. The confinement of gas precursors and of the particles toward the flow axis is achieved by a coaxial argon flow. Nucleated particles are kept entrained by the gas stream and collected in a removable tank at the exit of the reaction cell. Main process parameters are the nature of the gas (vapor) precursors, gas flow rates, pressure, as well as laser wavelength and laser power. For liquid precursors, the bubbled vapors are entrained into the reaction zone by a carrier gas.

Fe(CO)5/C2H4 and TiCl4/C2H4—were alternatively used as basic precursor mixtures for the preparation of iron and titanium oxide nanoparticles, respectively. In Figure 1, both these experimental arrangements are suggested. Additives such as air were employed for obtaining specific oxide nanostructures. In order to prevent the NaCl windows from being coated with powder, they were continuously flushed with Ar. Usually, either ethylene or argon was carrying through a bubbler the vapors of the liquid metal precursor into the reaction zone. In each of these systems, the installation for laser pyrolysis was adapted to the demands imposed by the nature of the precursors and the final aim of the synthesis process. In case of titania nanoparticles, a main variable trend was the change of a double nozzle system with a triple one (not shown in Figure 1) thus trying to avoid the direct reaction of TiCl4 with air.

2.4. Material Characterization

After synthesis, the morphology and composition of the iron oxides nanopowders were characterized by transmission electron microscopy (TEM), selected area electron diffraction (SAED), X-ray diffraction (XRD), and Mössbauer spectroscopy. The XRD pattern was recorded on a DRON DART UM-2 diffractometer equipped with a Cu Kα radiation and a graphite monochromator in the diffracted beam. The crystallite sizes were calculated from the corrected full width and half maximum (FWHM) applying the Debye-Scherrer formula. The powdery deposits were imaged in a transmission electron microscope Philips CM120ST (Customized Microscope 120 Super Twin, 120 kV max. acceleration voltage, about 2 A resolution, Cs = ~1.2 mm). The samples were analyzed by the different electron microscopy techniques such as Bright Field Transmission Electron Microscopy (BF-TEM), Selected Area Electron Diffraction (SAED) and High Resolution Transmission Electron Microscopy (HRTEM). 57Fe Mössbauer spectroscopy was used for analyzing the samples at temperatures ranging from 80 K to 230 K. Mössbauer spectra were collected in transmission geometry by inserting the sample in a bath liquid-nitrogen cryostat. A Mössbauer drive system operating in constant acceleration mode combined with conventional electronics and a 57Co (Rh matrix) source of about 25 mCi activity were employed.

3. Recent Examples of and Advances in the Preparation by Laser Pyrolysis of Oxide Semiconductor Particles

3.1. Spinel-Like Iron (III) Oxide (γ-Fe2O3)
3.1.1. The Preparation of the Nanoparticles and of Their Magnetic Fluids Counterparts

Nanoparticle Preparation
For producing nanosized iron oxide particles, the focused continuous-wave CO2 laser radiation (80 W maximum output power, λ = 10.6 μm) orthogonally crossed the gas flows emerging through two concentric nozzles (Figure 1). The gas mixture which contained air and Fe(CO)5 vapors (about 25 Torr vapor pressure at 20°C), entrained by C2H4, was admitted through the central inner tube. Iron oxide samples (labeled as 01 and 02) were obtained by varying the laser power between 35 W and 55 W as presented in Table 1. The other experimental conditions, namely, the reactor pressure, the relative flow of the oxidizing agent (air), and the flow of ethylene (as Fe(CO)5 carrier) were maintained constant (their values are displayed in Table 1).

Magnetic Fluid Preparation
The as-synthesized iron oxide nanopowders were used for the preparation of magnetic nanofluids. In what follows, the obtained magnetic fluid samples will be labeled MF01 and MF02 and are derived by dispersing in water samples 01 and 02, respectively. Water-based magnetic nanofluids are a special category of polar magnetic nanofluids showing particularities as concerning particle interactions and agglomerates formation. The synthesis of magnetic fluids has two main stages (1) preparation of nanosized magnetic particles, in particular by laser pyrolysis, and (2) subsequent stabilization/dispersion of the nanoparticles in water carrier. Electrostatic and steric stabilization procedures are both applicable for water-based magnetic nanofluids. Double layers steric + electrostatic (combined) stabilization of magnetic nanoparticles in water carrier was experimented recently using various chain length of carboxylic acid surfactants, as well as dodecyl benzensulphonic acid (DBS) [22]. In case of magnetic nanoparticles prepared by laser pyrolysis, a complementary difficulty appears due to the large agglomerates existing already in the nanopowder state, as a consequence of the magnetic dipolar interactions between uncoated nanoparticles. The sequence of steps of the preparation procedure for water-based magnetic nanofluids may be summarized as follows: (a) addition of NaOH (6N) to the water/magnetic nanopowder mixture in order to ensure a pH value of about 8.5–9, followed by heating up the reaction medium to about 75–80°C; (b) chemisorption of the surfactant (in the present case, lauric acid (LA)); (c) magnetic organosol; (d) magnetic decantation (elimination of residual salts); (e) correction of pH (using NaOH); (f) dispersion of surface-coated magnetic nanoparticles; (g) primary magnetic nanofluid; (h) magnetic decantation/filtration; (i) water-based magnetic nanofluid (diluted, with solid volume fraction of about 5%).

3.1.2. Nanoparticle Characterization

The XRD analysis of the as-synthesized nanopowders points to the presence of the spinel-like iron (III) oxide [10], namely, maghemite/magnetite iron phase (according to JCPDS 19-0629 for standard maghemite and JCPDS 39–1346 for maghemite). In Figure 2, a representative diffractogram obtained for the as-synthesized oxides is displayed. Although it refers to sample 01, its characteristic phase identification features are similar to that of sample 02 (not presented here). The unit-cell parameter (Table 1) was estimated from the 311 and 440 reflections. It presents relatively lower values to the standard magnetite value (Fe3O4 with a = 8.396 Å), suggesting the formation of a more likely maghemite phase (γ-Fe2O3). The broadness of the diffraction lines is associated with the formation of very small particles as well as with a high degree of structural/crystallographic disorder. The estimated mean crystallite dimension D (nm) is presented in Table 1. A higher crystallinity and slightly larger mean crystallite size may be deduced for the sample obtained at the higher laser power.

The identification of elements present in powders was performed using the energy dispersive analysis by X-rays (EDAX). The results are presented in the last column of Table 1. The stoichiometry, suggested by the relative quantities of oxygen and iron present in the synthesized powders, corresponds to a Fe3+ iron oxide, most probably maghemite. A rather low carbon contamination (about 10%), mainly due to the unwanted ethylene dissociation may be noticed. Although revealed by EDAX, the XRD analysis seems not able to reveal traces of carbon. It is worth to note that the sensitivity of this analysis is down to a few atomic percent and that low Z elements are detectable with limited sensitivity.

TEM analysis of samples 01 and 02 reveals an almost polycrystalline morphology (Figures 3(a), 3(b)). The nanoparticles show coalescent features. Cross-linked chains may be sometimes observed. An estimation of the particle mean sizes gives about 4.5 and 6 nm for samples 01 and 02, respectively.

The reflections revealed by the SAED analysis (Figure 4) may be attributed to a cubic structure of the iron oxide, namely, maghemite/magnetite. The strong diffraction ring at 0.25 nm may be noticed. Although difficult to distinguish between these phases from electron diffraction patterns alone, it is probable that maghemite prevails by referring to XRD results (see, e.g., the value of the estimated lattice parameter a in Table 1). Increased crystallinity seems to characterize the nanomaterial obtained at higher laser power. This can be considered as a consequence of both the higher temperature gradients in the reactions zone and the fast quenching of the condensed nanoparticles in the condensation zone. As revealed by the characterization methods employed, this process greatly favors maghemite phase in powders.

HRTEM analysis was performed on many different domains of the nanopowders and is presented in Figure 5. Nanocrystals with different orientation and mean diameters of about 5-6 nm are displayed in Figure 5(a). From the indicated squarish areas, the Fourier transform images are presented as insets. The left-side and the right-side groups of nanocrystals in Figure 5(a) display characteristics of the cubic structure of a maghemite crystal. The lattice fringes, corresponding to the (113) ( = 0.253 nm) and to the (220) ( = 0.313 nm) planes, are evidenced. A small distribution of d-values is caused by the imperfect crystallographic structure, probably due to the quenching of the material when leaving the reaction zone. The HRTEM image of Figure 5(b) presents agglomerated nanocrystals. They seem to be surrounded by an amorphous layer.

3.1.3. Magnetic Properties for the As-Synthesized Particles and for the Processed Magnetic Nanofluids

The magnetic properties of the samples were studied by temperature-dependent Mössbauer spectroscopy. The 80 K Mössbauer spectra of the analyzed samples are shown in Figure 5. The derived probability distributions of the hyperfine field are presented at the right side. The narrow peak of the distribution, centered at about 52 T, evidences the presence of mainly maghemite in sample 01. The larger distribution peak centered at about 48 T in sample 02 might have two different reasons: (i) a starting magnetic relaxation process already present at 80 K and (ii) a much defected structure shifting structurally from maghemite to magnetite (the average magnetic hyperfine field of magnetite being lower than the one of maghemite). The magnetic relaxation process was analyzed [23] in terms of the collapsing behavior of the Mössbauer spectra at higher temperatures. From the Mossbauer spectra obtained at different temperatures, blocking temperatures of about 400 K and 200 K were derived for samples 01 and 02, respectively. Particle average sizes of about 9 nm for sample 01 and, respectively, 7 nm for samples 02 were estimated, starting from the above-mentioned blocking temperatures and considering noninteracting nanoparticles.

The ferrofluids obtained by dispersing the nanopowders in water showed blocking temperatures of 230 K and 200 K for samples MF01 and MF02, respectively. It is worth mentioning that the higher blocking temperature observed for 01 as compared to MF01 is most probably generated by nonnegligible interparticle interactions in the powder sample (e.g., the substantial presence of maghemite with its ferri-magnetic behavior). In the defected maghemite-magnetite mixtures (sample 02), a spin-glass-like structure with reduced (almost negligible) net magnetic moment per particle seems to be present, affecting/reducing drastically the magnetic dipolar interactions, even in the powder form. The best magnetic performances (a maximum amount of magnetic nanoparticles at room temperature and related highest magnetization) correspond to the ferrofluid obtained by dispersing the well-formed maghemite-based nanoparticles synthesized under a laser power of 55 W.

The reduced magnetization curves of the as-synthesized nanopowders are presented in Figure 7. It is worth mentioning that none of the samples is saturated at the maximum available field of 1.1 T. This behavior can be considered an additional evidence for the disordered spin configuration, connected with the defected structure inside nanoparticles, in agreement with the Mössbauer data. Therefore, the reduced magnetization curves for the two samples were obtained with respect to the specific magnetization at the maximum field (denoted as ). The magnetization of the 01 sample, 50 emu/g, is much greater than for sample 02 (15 emu/g) supporting a three times larger magnetic moment per particle in sample 01 as compared with sample 02 in the assumption that the particle mean sizes of the two samples are almost similar. On the other hand, the reduced magnetization of sample 01 at very low field is clearly larger than that of sample 02, providing evidence for a larger amount of magnetic state at room temperature in this sample in agreement with the larger blocking temperature evidenced by Mössbauer spectroscopy.

Following the procedures described in a previous section, the iron oxide nanopowders were subsequently synthesized as water-based magnetic fluids (MFs). TEM analysis of the ferrofluids showed that depending on the nanopowder synthesis parameters, different degrees of agglomeration are still present. The morphology of samples MF01 and MF02 may be examined in Figures 8(a) and 8(b). The nanoparticles exhibit a spherical shape, confirmed by the 0.86 value of the form factor. From SAED analysis (no presented here), an iron oxide cubic structure is deduced, with lattice constants of 0.835 nm and 0.837 nm for MF01 and MF02, respectively. This estimation may indicate that the maghemite-like structure is favored in the ferrofluid-derived from the sample synthesized at high laser power. On the other hand, one may observe that the MF prepared from 02 nanoparticles (Figure 8(b)) presents a slightly lower degree of agglomeration as compared with MF02 (Figure 8(a)). The suppression of interparticle interaction in sample MF01 could be less effective, in spite of the fact that insignificant magnetic relaxation differences separate the MF samples.

The reduced magnetization curves of the ferrofluid samples MF01 and MF02, synthesized from the powders 01 and 02, respectively, are shown in Figure 9. The dependencies of the reduced magnetizations versus the applied magnetic field are quite similar to the ones of the powder samples. A major difference concerns the values of the magnetization, , at the maximum field of 1.1 T. This time these are expressed in emu/cm3 (or A/m) in order to take into account the inhomogeneous character of the ferrofluid, seen as a liquid-solid composite ( given in emu/cm3 derives from the specific magnetization in emu/g times the ferrofluid density, in g/cm3). The value in sample MF01 is almost 7 times larger than the value in sample MF02, proving clearly the better magnetic performances of the ferrofluid derived from the 01 powder sample. In addition, one observes that the low field part of the reduced magnetization in the magnetic fluid sample MF01 is lower than for the 01 sample and that a certain amount of suparparamagnetic phase is to be found in this sample even at 1.1 T. Therefore, due to the cancellation of interparticle interactions, the magnetometry data infer that the magnetic relaxation at room temperature has to be more advanced in the MF01 ferrofluid sample as compared with the 01 powder sample (in agreement with the Mossbauer data showing a lower blocking temperature in the ferrofluid). Hence, the magnetic relaxation may hide the information about the static spin disorder. The specific magnetizations are not strictly related to the different degree of spin disorder in the samples but, at least qualitatively, the magnetometry results, in agreement with the Mossbauer ones, support very well the conclusion that the lowest spin disorder is present in the 01 sample and in the corresponding MF01 ferrofluid.

3.2. Titania, with Major TiO2 Anatase Phase
3.2.1. Particle Preparation and Characterization

The synthesis of TiO2 nanopowder was performed by employing a modified version of the pyrolysis setup [24] in which TiCl4 and air, as gas-phase precursors, are simultaneously allowed to emerge into the flow reactor (see also Figure 1). Ethylene served as a carrier for the TiCl4 vapors and as an energy transfer agent. A special irradiation geometry employing a central triple nozzle system was used. The focused IR radiation (400 W nominal power) was intersecting at right angles the reactant flows. During all experiments, the total pressure in the reactor was held at 550 mbar.

The samples (labeled SN, SA, and S0) are studied relatively to the input variation of their oxygen precursors. Sample SN was obtained by replacing air with nitrous oxide. A much lower air flow was used to obtain sample SA as compared to sample S0. The main experimental parameters are listed in Table 2. In the last columns of the table are gathered the mean crystallite sizes [25] as well as the lattice parameters (a,c) as extracted from the XRD patterns (see below).

The obtained titanium oxide nanostructures were characterized by XRD, TEM, and SAED.

XRD phase analysis (Figure 10 and the last columns of Table 2) reveals an overwhelming dominancy of the anatase phase (more than about 92%) in the sample S0, obtained at the highest air precursor concentration. It was already observed [26] that for titania produced by RF thermal plasma, rutile formation is favored by oxygen-deficient gas-phase TiO2 clusters while anatase tends to condense from oxygen-rich clusters. We should mention that for both air and nitrous oxide, at lower air flows (e.g., 10 sccm for sample SN), the powder was gray with slight blue parts. At high air input flows (150 sccm for sample S0), the color of the powder becomes light yellow to white. Some salient features characterize the SN, SA, and S0 series: (i) the significant decrease of the mean particle sizes for SN and SA relatively to S0, particularly concerning the rutile phase; and (ii) the decrease of the total amount of the TiO2 phases relatively to the S0 sample, especially in case of the anatase phase. For the TiO2 SA sample, anatase percentage is approximately 74%, which is quite close to the well-known Degussa P25 commercial sample.

Low-magnification TEM micrographsfor TiO2 samples SN and SA (Figure 11) show groups of loosely-bound aggregated nanoparticles.

The SAED patterns for samples SA and S0 are presented in Figure 12. The identification of the interplanar distances is indicated by arrows and these qualitative results can be directly compared with those obtained by means of XRD. In general, SAED analysis confirms that the titania nanoparticles are a mixture of anatase and rutile. However, increased crystallinity and dominant anatase phase are found for the reference sample (S0). We should note that the diffusivity observed in the SAED pattern of sample SA could be due not only to an amorphous material but also to the increased number of crystalline nanometer-sized particles [27]. The most intense diffraction rings can be assigned to the (101) anatase (at 3.52 Å) and (110) rutile (at 3.25 Å). Some rings may appear by a superposition of anatase and rutile reflections, such as the rings at 2.48 Å  and 1.68 Å. In case of the better crystallinity of sample S0, the complementary ring at 1.4 Å  (corresponding to rutile (007) and anatase (204)) is identified.

In Figure 13, a comparative TEM analysis for medium- (a, c, and e) and high-resolution (b, d, and f) images of SN, SA and S0 titania samples is performed. At a higher magnification, the TEM micrographs of samples discussed in this work exhibit both round-shaped and elongated or facetted particles with irregular shapes and sizes (Figures 13(a)13(f)). Primary nanocrystals seem to be often present. In Figure 13(b), an isolated SN primary nanocrystal is presented, showing an elongated (about 15 nm) shape. Particles surrounded by an amorphous layer (Figures 13(a) and 13(c)) appear in sample SN and SA, respectively. The rather well-defined microcrystallites of sample S0 exhibit irregular, mostly polyhedral shapes (Figure 13(f)).

4. Conclusions

Recent results obtained in the preparation of gamma iron oxide (γ-Fe2O3) and titania (TiO2) semiconductor nanostructures using the laser pyrolysis method are outlined. The properties of different nanometric iron oxides prepared by laser pyrolysis were analyzed from the point of view of their morphology and magnetic behavior. The nanoparticles are characterized by a cubic maghemite/magnetite structure. Maghemite phase seems to prevail in the nanopowders obtained at the highest laser power. These nanoparticles also present a better crystallinity and slightly larger mean crystallite dimensions. The analysis of samples as water-based nanofluids shows that the best magnetic performances (a maximum amount of magnetic nanoparticles at room temperature and related highest magnetization) correspond to the ferrofluid derived from maghemite-based nanoparticles synthesized under a higher laser power.

TiO2 nanoparticles comprising a mixture of anatase and rutile phases were synthesized via the sensitized laser pyrolysis of TiCl4- (vapors) based gas-phase mixtures. TiO2 samples were obtained by varying the amount of oxidizing agent (air). Enhanced crystallinity and larger crystallite mean sizes are observed at increased amount of the oxidizing agent. Samples with a major concentration of anatase phase (about 90%) were obtained by the same technique by using as precursors very high air flows.


This work was supported by the Romanian Education Ministry through CEEX (Project no. S2/C8/2005), PNCD2 (71/083/2007), and NUCLEU: LAPLACE 2 (PN 06 36/2008) programs.