“…23 The low symmetry of the Mössbauer signal at the central position in Fe-doped TiO 2 (B) is due to the presence of more oxygen vacancies-Fe dipoles interaction compared to Fe-doped anatase nanorods. 24 The absence of any sextet in fit-derived Mössbauer spectra clearly showed that the ferromagnetic component in the samples is not due to metallic iron and iron oxide. 25 Fig .…”
Fe-doped TiO2(B) and anatase phases were synthesized at different thermal treatment conditions using Fe-doped hydrogen titanate nanorods as a precursor. X-ray diffraction, Raman and Mössbauer studies ruled out the formation of secondary phase of either metallic Fe or iron oxide cluster in the samples and confirmed the ferromagnetism have originated from the defects. Mössbauer spectroscopy studies show a doublet and measured isomer shifts support the high spin Fe3+ charge state occupying the Ti4+ sites with associated changes in local lattice environment. The magnetization at room-temperature of the TiO2(B) sample is 0.020 emu/g whereas that of anatase sample is 0.015 emu/g. The decrease of magnetization with the structural phase transformation from TiO2(B) to anatase is attributed to the reduction in number of defects (oxygen vacancy) during the transformation process. Existence of these defects was further supported by the photoluminescence measurements
“…23 The low symmetry of the Mössbauer signal at the central position in Fe-doped TiO 2 (B) is due to the presence of more oxygen vacancies-Fe dipoles interaction compared to Fe-doped anatase nanorods. 24 The absence of any sextet in fit-derived Mössbauer spectra clearly showed that the ferromagnetic component in the samples is not due to metallic iron and iron oxide. 25 Fig .…”
Fe-doped TiO2(B) and anatase phases were synthesized at different thermal treatment conditions using Fe-doped hydrogen titanate nanorods as a precursor. X-ray diffraction, Raman and Mössbauer studies ruled out the formation of secondary phase of either metallic Fe or iron oxide cluster in the samples and confirmed the ferromagnetism have originated from the defects. Mössbauer spectroscopy studies show a doublet and measured isomer shifts support the high spin Fe3+ charge state occupying the Ti4+ sites with associated changes in local lattice environment. The magnetization at room-temperature of the TiO2(B) sample is 0.020 emu/g whereas that of anatase sample is 0.015 emu/g. The decrease of magnetization with the structural phase transformation from TiO2(B) to anatase is attributed to the reduction in number of defects (oxygen vacancy) during the transformation process. Existence of these defects was further supported by the photoluminescence measurements
“…Recently, Erdem et al . have reported that, the additional resonance at the g‐factor value of ~2.0 corresponds to the Fe 3+ ‐exchange coupled magnetic secondary phase.…”
Section: Electron Paramagnetic Resonance Studiesmentioning
The changes in the ferroelectric and magnetic properties of the nanostructured Pb(Zr0.52Ti0.48)1‐xFexO3 (0 ≤ x ≤ 0.06) due to the doping of different amounts of acceptor ions (Fe3+) have been studied. X‐ray diffraction studies show that the system maintains the tetragonal phase up to the doping of 2 mol% of Fe3+ and the formation of secondary phase magnetoplumbite (PbFe12O19) on further doping. Electron paramagnetic resonance studies have revealed the formation of defect centers which in turn arise due to the interaction of Fe3+ ions with oxygen vacancies, which are generated in the lattice. This results in the appearance of room temperature ferromagnetic (RTFM) behavior in the doped samples. The dielectric studies reveal that with the concentration of Fe3+ the peak near the maxima of dielectric constant (ε′m) is broadened. Studies of the defect dipoles on the ferroelectric properties have been performed by polarization measurement. The variations of the above properties with the structural and morphological features of the samples have also discussed.
“…However, taking into account Refs. and , in our opinion, small quantities of Fe 2 O 3 at the Fe/PZT interface could be considered as a dopant for PZT material. The acceptor Fe 3+ ions could form alignable and immobile defect dipoles, oxygen vacancies–Fe 3+ ions, which, according to Refs.…”
Section: Resultsmentioning
confidence: 81%
“…The acceptor Fe 3+ ions could form alignable and immobile defect dipoles, oxygen vacancies–Fe 3+ ions, which, according to Refs. and , increase the performance of the PZT material. A key role of the FeO monolayer for ME coupling mechanism at the PZT/Fe interface, similar to those reported in the case of the BaTiO 3 /Fe interface , is expected to be evidenced in the future.…”
A new method to fabricate an Fe–PZT core–shell wire arrays developed in three steps is reported in this paper. This involves the electrochemical growth of an iron wire array by template method, deposition by spin coating of the PZT precursor prepared by sol–gel technique on the iron wires surface and annealing treatment to obtain Fe–PZT core–shell structures. The structure of the Fe–PZT core–shell wire array was characterized by scanning electron microscopy (SEM) and Raman scattering. Raman lines situated at 372 and 575 cm−1 indicate the formation of the FeO particles on the Fe wires surface as a result of the use of an aqueous solution for electrochemical synthesis. An upshift of Raman lines of Fe decorated with FeO wires was observed after formation of Fe–PZT core–shell structure. The annealing treatment of this structure involves a partial transformation of the FeO into Fe2O3 particles both with structure rhombohedral and cubic that were evidenced by Raman lines peaked at 243 and 497 cm−1, respectively.
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