preparation and properties of magnetic iron oxide nanotubes

A vailable online at www.sciencedirect.com Particuology 6 (2008) 334–339 Preparation and properties of magnetic iron oxide nanotubes Baoliang Lv a,b , Yao Xu a,∗ , Dong Wu a , Yuhan Sun a a State Key Laboratory of Coal Conversion, Institute of Coal Chemistry, Chinese Academy of Sciences, Taiyuan 030001, China b Graduate University of the Chinese Academy of Sciences, Beijing 100039, China Received 7 March 2008; accepted 4 April 2008 Abstract Magnetite (Fe 3 O 4 ) nanotubes were prepared by reducing synthesized hematite (␣-Fe 2 O 3 ) nanotubes in 5% H 2 +95% Ar atmosphere, and then maghemite (␥-Fe 2 O 3 ) nanotubes were obtained by re-oxidizing the Fe 3 O 4 nanotubes. The nanotube structure was kept from collapsing or sintering throughout the high temperature reducing and re-oxidizing processes. The coercivities of the Fe 3 O 4 and ␥-Fe 2 O 3 nanotubes synthesized were found to be 340.22 Oe and 342.23 Oe, respectively, both higher than other nanostructures with the same phase and of similar size. Both adsorbed phosphate and the nanotube structure are considered responsible for this high coercivity. © 2008 Chinese Society of Particuology and Institute of Process Engineering, Chinese Academy of Sciences. Published by Elsevier B.V. All rights reserved. Keywords: Nanostructures; Iron oxides; Nanotubes; Magnetic properties 1. Introduction Magnetic materials with special nanostructures are scientif- ically interesting and technologically important in research for future applications (Sui, Skomski, Sorge, & Sellmyer, 2004a). Iron oxides as an important class of magnetic materials have been widely used in catalysis (Zhang et al., 2005), magnetic devices (Zeng, Li, Liu, Wang, & Sun, 2002), environment pro- tection (Wu, Qu, & Chen, 2005), sensors (Sun, Yuan, Liu, Han, & Zhang, 2005), drug delivery (Wu et al., 2007) and water split- ting (Cesar, Kay, Gonzalez Martinez, & Grätzel, 2006). Up to now, iron oxides with nanostructures have attracted a great deal of attention because of their promising properties and appli- cations. Many iron oxide particles with zero-, one-, two- and three-dimensional (0D, 1D, 2D and 3D) nanostructures have been synthesized. Ferromagnetic nanotubes were considered as candidates for recording head, biomagnetic sensors, cata- lysts, etc., because of their expected vortex magnetization state and floatability in liquid as a result of their hollow structure (Goldstein, Gelb, & Yager, 2001; Haberzettl, 2002; Khizroev, Kryder, Litvinov, & Thomson, 2002). Iron oxide nanotubes have been synthesized mostly via the so-called template-directed growthmethod.For example, Sui, Skomski, Sorge, and Sellmyer ∗ Corresponding author. Tel.: +86 351 4049859; fax: +86 351 4041153. E-mail address: xuyao@sxicc.ac.cn (Y. Xu). (2004b), Wang, Wang, Li, Xu, and Zhou (2006), and Shen et al. (2004) used porous anodic aluminium oxide (AAO) as tem- plate to prepare Fe 3 O 4 and ␣-Fe 2 O 3 nanotube arrays; Sun et al. (2005) used carbon nanotubes as templates to fabricate ␣- Fe 2 O 3 nanotubes; Liu et al. (2005) used MgO nanowires as templates to fabricate single-crystal Fe 3 O 4 nanotubes. How- ever, templates not only introduced extraneous impurities but also increased production cost, not to say the many prob- lems to prepare these materials at large scale. Therefore, it is of practical significance to develop a template-free and somewhat easier method to synthesize magnetic iron oxides nanotubes. Recently, Jia et al. (2005) synthesized ␣-Fe 2 O 3 nanotubes by a hydrothermal method without using template. In this work, we improved their work by first synthesizing ␣-Fe 2 O 3 nanotubes, followed by reducing ␣-Fe 2 O 3 and re-oxidizing the Fe 3 O 4 to ␥-Fe 2 O 3 nanotubes. The magnetic properties of the Fe 3 O 4 and ␥-Fe 2 O 3 nanotubes were investigated by using vibrating sample magnetometry (VSM). 2. Experimental All the reagents were A.R. grade and were used in prepara- tion without further purification: ferric chloride (FeCl 3 ·6H 2 O, China Medicament Co.), sodium dihydrogen phosphate (NaH 2 PO 4 ·2H 2 O, Tianjin Chemical Reagent Co.), double- 1674-2001/$ – see inside back cover © 2008 Chinese Society of Particuology and Institute of Process Engineering, Chinese Academy of Sciences. Published by Elsevier B.V.All rights reserved. doi:10.1016/j.partic.2008.04.006 B. Lv et al. / Particuology 6 (2008) 334–339 335 distilled water. Reduction gas was composed of 5 v% H 2 (high purity) and 95 v% Ar (high purity). The preparation of ␣-Fe 2 O 3 nanotubes was an improved approach based onliterature (Jia et al., 2005).In a typical synthe- sis, 40 mL of FeCl 3 aqueous solution (46.2 mmol/L) and 40 mL of NaH 2 PO 4 aqueous solution (1.9 mmol/L) were first mixed and then dispersed uniformly by ultrasonic irradiation. The solu- tion was then sealed in a 100-mL Teflon-lined stainless steel autoclave and hydrothermally treated for 36 h at 240 ◦ C. At last, a red precipitate was obtained at the bottom of the autoclave and was separated by centrifugation. The precipitate was washed three times with distilled water, and then dried at 60 ◦ C in air. The resulting powder was ␣-Fe 2 O 3 nanotubes, named as S1. Fe 3 O 4 nanotubes were obtained by reducing S1 in a tubular oven at 500 ◦ Cfor2.5hina5%H 2 +95% Ar atmosphere, and the resulting black powder was named as S2. In this process, the temperature and reduction time were very important, or else ␣-Fe 2 O 3 or FeO would be present in the reduction product. To prepare ␥-Fe 2 O 3 nanotubes, the as-prepared Fe 3 O 4 nanotubes were oxidized by air at 300 ◦ C for 2 h, to produce a red powder, named as S3. X-ray diffraction (XRD) measurement was performed on a D8 Advance Bruker AXS diffractometer using Cu K␣ radia- tion (λ=1.5406 Å). Raman spectra were recorded using a Horiba Labram HR800 spectrometer equipped with a Spectra Physics 514 nm argon ion laser. The morphologies of the samples were observedbyscanningelectronmicrograph(SEM,LEO 1530VP) and transmission electron micrograph (TEM, Hitachi H-600). X-ray photoelectron spectroscopy (XPS) measurements were performed on a PHI 5300× multi-technique system with Mg K␣ X-ray source (PerkinElmer Physical Electronics).Magnetichys- teresis loops were measured by vibrating sample magnetometry (VSM, Lakeshore 7407). 3. Results and discussion Fig. 1 shows the XRD patterns of samples S1 (a), S2 (b) and S3 (c). In Fig. 1(a), the initial synthesized product (sample S1) Fig. 1. XRD patterns of samples S1 (a), S2 (b) and S3 (c). Fig. 2. Raman spectra of samples S2 (a) and S3 (b). can be exclusively indexed to ␣-Fe 2 O 3 , according to standard data (JCPDS 33-0664). In Fig. 1(b) and (c), the reflection peaks of XRD patterns of S2 and S3, can be well assigned to a spinel structure with the characteristic reflections of ␥-Fe 2 O 3 (JCPDS 39-1346) or Fe 3 O 4 (JCPDS 19-0629). However, it is well-known that clear identification of ␥-Fe 2 O 3 and Fe 3 O 4 based on ordi- nary XRD pattern is an arduous task due to their same spinel structure and their similar lattice parameters (Xiong, Ye, Gu, & Chen, 2007). Although the color of S2 was black and S3, red, corresponding to Fe 3 O 4 and ␥-Fe 2 O 3 , respectively, the purity of the samples cannot be simply identified by their appearance. To differentiate samples S2 and S3 clearly, further characteriza- tion is needed for more convincing evidence, for which Raman spectrum was resorted to (Daou et al., 2006; Pinna et al., 2005; Xiong et al., 2007). A representative Raman spectrum of sam- ple S2, shown in Fig. 2(a), exhibits two clear peaks at 665 and 540 cm −1 , which can be indexed to the A1g and T2g transitions of the Fe 3 O 4 phase (Shebanova & Lazor, 2003). In Fig. 2(b), the Raman spectrum of sample S3, the different characteristic bands of ␥-Fe 2 O 3 (700, 500 and 350 cm −1 ) can be observed (Varadwaj, Panigrahi, & Ghose, 2004). Consequently, it should be reasonable to think that sample S2 is Fe 3 O 4 and sample S3 is ␥-Fe 2 O 3 . Fig. 3 presents the SEM and TEM images of samples S1, S2 and S3. Fig. 3(a) and (b) show the morphologies of ini- tial synthesized ␣-Fe 2 O 3 nanotubes (sample S1), in which the nanotubes can be seen clearly, with length of 160–300 nm, 336 B. Lv et al. / Particuology 6 (2008) 334–339 Fig. 3. SEM and TEM images of ␣-Fe 2 O 3 nanotubes in sample S1 (a and b), Fe 3 O 4 nanotubes in sample S2 (c and d) and ␥-Fe 2 O 3 nanotubes in sample S3 (e and f). B. Lv et al. / Particuology 6 (2008) 334–339 337 and outer and inner diameters of 70–120 nm and 45–80 nm, respectively. Fig. 3(c) and (d) show the morphologies of Fe 3 O 4 nanotubes (sample S2), with their well retained nanotube struc- ture. Fig. 3(e) and (f) show the nearly same morphologies of ␥-Fe 2 O 3 (sample S3) together with their well retainedtubestruc- ture. Fig. 3(d) and (e) show that there was no obvious change in the length and diameter of the nanotubes. Comparison of the TEM images of the three samples indicates that the Fe 3 O 4 and ␥-Fe 2 O 3 nanotubes are conglomerated with each other, while ␣-Fe 2 O 3 nanotubes are well dispersed, apparently due to the mutual attraction of the magnetic Fe 3 O 4 and ␥-Fe 2 O 3 particles, though no obvious difference can be found from the morpholo- gies of the three samples. Generally, nanostructures areoften destroyed due to sintering or collapsing during treatment at high temperature. But Fig. 3 showsthatthenanotubestructurewas well preserved after reduc- tion and re-oxidization at high temperature. There might be two reasons for this. First, according to Jiao et al. (2006), conversion of ␣-Fe 2 O 3 to Fe 3 O 4 involves a change from a hexagonal close- packed oxide ion array (␣-Fe 2 O 3 ) to a cubic close-packed array (Fe 3 O 4 ). This conversion is not merely topotactic, but involves a sheave of oxide ion planes from AB to ABC stacking, and this significant structural change can occur without much destroy- ing the tube structure. The thin walls of the nanotubes endowed the solids with a structural flexibility that made such solid/solid transformation smooth while preserving the tube structure. Sec- ond, according to Jia et al. (2005), phosphate could be adsorbed on ␣-Fe 2 O 3 by reacting with the singly coordinated surface hydroxy groups to form a monodentate orbidentate inner-sphere complex. Here, the amount of adsorbed phosphate was so small that it could not be detected by XRD. To confirm the existence of phosphate on the surface of the nanotubes, XPS analysis was carried out on the surface element composition of the initial ␣- Fe 2 O 3 nanotubes, with the result shown in Fig. 4(a). The binding energies obtained in the XPS analysis were corrected by refer- encing the C1s line to 284.5 eV. Seen from Fig. 4(a), the binding energy of P2p was found at 133.6 eV in the spectrum, which agreed with the reported value of PO 4 3− (Wang et al., 2003). To further identify the existence of the phosphate layer, a high- magnification image of sample S1 was obtained on TEM, as shown in Fig. 4(b), indicating the presence of a 2.5-nm adsorp- tion layer, thus confirming the presence of a phosphate layer on the surface of synthesized ␣-Fe 2 O 3 nanotubes. The adsorbed phosphate would be very stable in the reduction process, and act as a framework or a protection shell for the nanotubes. When the reduction of ␣-Fe 2 O 3 went on, the phosphate on the surface could not be reduced, and only the inner ␣-Fe 2 O 3 wasreducedby hydrogen. Therefore, the nanotubes could be kept from sintering or collapsing. To confirm the stabilization of phosphate on nan- otubes, pure iron phosphate (FePO 4 ) sample was treated under the same reduction condition as that for ␣-Fe 2 O 3 reduction. The XRD pattern (not given here) of the reduction product showed that FePO 4 was reduced to Fe 2 PO 5 . Oxidation of Fe 3 O 4 nan- otubes to ␥-Fe 2 O 3 nanotubes involved a decrease in the number of Fe atoms per unit cell of 32 oxygen ions, from 24 in Fe 3 O 4 to 21(1/3) in ␥-Fe 2 O 3 . This reaction proceeded with outward migration of the Fe 2+ cations towards the surface of the crystal Fig. 4. (a) XPS spectrum of ␣-Fe 2 O 3 nanotubes and (b) high magnification TEM image of a nanotube in sample S1. together with the creation of cation vacancies and the addition of oxygen atoms. At the surface the Fe 2+ cations were oxidized through interacting with adsorbed oxygen to form of ␥-Fe 2 O 3 , too. The whole process involved a topotactic reaction in which the original crystal morphology was preserved throughout the process (Cornell & Schwertmann, 2003). Magnetic nanoparticles, especially those with special struc- tures, often exhibit unusual magnetic behaviors different from that of bulk solids, owing to finite size effects and microstructure (Bødker, Hansen, Bender Koch, Lefmann, & Mørup, 2000). To investigate the magnetic properties of the as-synthesized nan- otubes, magnetic hysteresis (M–H) loop measurements were carried out in an applied magnetic field at room temperature, with the field sweeping from −18 to 18 kOe. Fig. 5 shows the M–H loops of Fe 3 O 4 (a) and ␥-Fe 2 O 3 (b) nanotubes at room temperature. From Fig. 5(a), the M–H loop of Fe 3 O 4 nanotubes shows ferromagnetic behavior with a saturation mag- netization (Ms) of 60.92 emu/g, a remanent magnetization (Mr) of 18.56 emu/g and a coercivity of 340.22 Oe at room tem- perature. Compared to bulk Fe 3 O 4 (Ms = 92 emu/g, coercivity 115–150 Oe) (Liu, Fu, & Xiao, 2006), the Ms was obviously lower and the coercivity was obviously higher. Fe 3 O 4 nanotubes also possess higher coercivity than other Fe 3 O 4 nanostruc- tures of similar size, such as octahedral nanoparticles (141 Oe), nanocubes (62 Oe) and hollow spheres (40 Oe) (Daou et al., 2006; Huang & Tang, 2005; Xiong et al., 2007; Yu et al., 2006). From Fig. 5(b), the M–H loop of ␥-Fe 2 O 3 nanotubes shows ferromagnetic behavior with a Ms of 42.71 emu/g, a Mr of 338 B. Lv et al. / Particuology 6 (2008) 334–339 Fig. 5. M–H loops of Fe 3 O 4 nanotubes (a) and ␥-Fe 2 O 3 nanotubes (b). The inset diagrams are their corresponding expanded low-field curves. 13.56 emu/g and a coercivity of 342.23 Oe at room temperature. Compared to bulk ␥-Fe 2 O 3 (Ms = 76 emu/g, coercivity 300 Oe) (Zhang, Tang, and Hu, 2008), the Ms is obviously lower and the coercivity is somewhat higher. Similar to Fe 3 O 4 nanotubes, ␥-Fe 2 O 3 nanotubes also have a higher coercivity than other reported ␥-Fe 2 O 3 nanostructures, such as nanofibres (78.11 Oe), nanoparticles (106 Oe), and some reported superparamagnetic ␥-Fe 2 O 3 particles (0 Oe) (Han et al., 2007; Jing, 2006; Zhang et al., 2008). It is noted that boththesetwo magneticironoxidenan- otubes have a higher coercivity than other nanostructures with the same phase and of similar size. Furthermore, the M–H loops of Fe 3 O 4 nanotubes and ␥-Fe 2 O 3 nanotubes indicate the similar magnetic domain type. On the basis of the criteria given by Dun- lop (Cornell & Schwertmann, 2003), the Mr/Ms value should be larger than 0.5 for single domain (SD) particles, between 0.1 and 0.5 for pseudosingle-domain (PSD) particles and lower than 0.1 for multidomain (MD) particles. From Fig. 5, both the two samples possess PSD-type magnetic domains, and their Mr/Ms values are 0.30 and 0.32, respectively. There might be two reasons for the high coercivity. First is the influence of adsorbed phosphate at the surface of these nan- otubes, which has been confirmed previously by XPS, and the phosphate is not a magnetic material. From Fig. 5, both the two samples have a Mr/Ms value between 0.1 and 0.5, indicating that they may possess the magnetic properties of SD and MD struc- tures simultaneously. If the synthesized products possess more properties of MD structures, the magnetic domain walls would exist inside the particles. For MD materials, the movement of magnetic domain walls is the main reason for coercivity. It is well known that there exist surface domain walls for MD par- ticles. Here, the surface domain walls should be present at the interface between iron oxide and the adsorbed phosphate. The phosphate as an uninterrupted adsorbed layer can easily block the movement of the surface domain walls and result in domain wall pinning, which contributesto the high coercivity. Even if the synthesized products possess more properties of SD particles, the coercivity would also increase. For SD magnetic material, magnetic domain wall does not exist, and spin flip conversion is mainly responsible for the coercivity. In this case, the coor- dination bonds between adsorbed phosphate ions and iron ions would form spin pinning and block spin flip conversion, directly resulting in the increase of coercivity of the samples. Second, the nanotube structure may be another reason for the high coerciv- ity. Torres-Heredia, López-Urías, and Mu ˜ noz-Sandoval (2005) simulated the micromagnetic property of iron nanorings, and they found large coercive fields for d in /d out > 0.5 (d in and d out are the inner and outer diameters of the rings, respectively) and t = 160–200 nm (t is the thickness of the rings or length of the tubes) nanorings due to the absence of the vortex states and the presence of out-plane and in-plane spin configurations. In our samples, the average d in /d out valueof nanotubes isabout 0.7, and the length of many nanotubes is about 200 nm, which snugly fall into the thickness range of nanorings mentioned in the literature (Torres-Heredia et al., 2005). So the nanotubes can be thought as nanorings with immensely large thickness, and this structure can contribute to the high coercivity. 4. Conclusions Fe 3 O 4 nanotubes were prepared by reducing synthesized ␣- Fe 2 O 3 nanotubes with a gas mixture of 5% H 2 +95% Ar at 500 ◦ C for 2.5 h, and then ␥-Fe 2 O 3 nanotubes were obtained by re- oxidizing the Fe 3 O 4 nanotubes with air at 300 ◦ C for 2 h. The nanotube structure was well retained without collapsing or sin- tering, for which, adsorbed phosphate and the type of crystal structure conversion should be the two most important reasons. 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