Hydrothermal phase transformation of hematite to magnetite

  • Jie-feng Lu1 and

    Affiliated with

    • Cho-Jen Tsai1Email author

      Affiliated with

      Nanoscale Research Letters20149:230

      DOI: 10.1186/1556-276X-9-230

      Received: 7 March 2014

      Accepted: 13 April 2014

      Published: 13 May 2014


      Different phases of iron oxide were obtained by hydrothermal treatment of ferric solution at 200°C with the addition of either KOH, ethylenediamine (EDA), or KOH and EDA into the reaction system. As usually observed, the α-Fe2O3 hexagonal plates and hexagonal bipyramids were obtained for reaction with KOH and EDA, respectively. When both KOH and EDA were added into the reaction system, we observed an interesting phase transformation from α-Fe2O3 to Fe3O4 at low-temperature hydrothermal conditions. The phase transformation involves the formation of α-Fe2O3 hexagonal plates, the dissolution of the α-Fe2O3 hexagonal plates, the reduction of Fe3+ to Fe2+, and the nucleation and growth of new Fe3O4 polyhedral particles.


      Iron oxides Hydrothermal Phase transformation


      The more stable phases in iron oxides are hematite and magnetite. Hematite can be used in a lot of applications, such as sensors [1], water photooxidation [2], drug delivery [3], lithium ion battery [4], pigmentation [5], solar cell [6], etc., and magnetite can be utilized in biomedicine [711], magnetic devices [12], etc. Therefore, studies about the nano/microstructures of iron oxides and their properties, which are related to the intrinsic structure and crystal shapes, have been intensively engaged, especially for hematite and magnetite. The bandgap of hematite is 2.0 to 2.2 eV which makes it useful in applications that involve visible light absorption [13, 14]. Magnetite has unique electric and magnetic properties because its intrinsic crystal structure allows electrons to be transferred between Fe2+ and Fe3+ in the octahedral sites [15].

      Many researches have demonstrated the capability of using chemical syntheses to control particle morphologies of iron oxide by surfactants [1618]. Morphologies like wires [19], rods [20], tubes [21], rings [22], disks [23], cubes [24], spheres [25], hexagonal plates of α-Fe2O3 [26, 27], and polyhedral particles of Fe3O4 [28, 29] have been synthesized successfully.

      Several robust methods have been developed for phase transformation of iron oxides. α-Fe2O3 can be transformed to Fe3O4 at high temperature under a reducing ambient, such as hydrogen ambient [30, 31]. Yanagisawa and Yamasaki also showed that by controlling the mineralizer solutions, temperatures, and partial pressures of hydrogen in a hydrothermal system, phase transformation from α-Fe2O3 to Fe3O4 particles can be achieved [32]. The result indicated that high temperature and high pressure of hydrogen can accelerate the reduction reaction.

      Phase transition of iron oxides can also take place by hydrothermal reaction with a reducing agent [33, 34]. Sapieszko and Matijewic had observed a similar phase transformation from α-Fe2O3 hexagonal plates to octahedral Fe3O4 particles triggered by the addition of hydrazine which is used as an antioxidant [35] during hydrothermal process.

      In this experiment, we explore the role of ethylenediamine (EDA or en in ligand form) on the phases of iron oxide in hydrothermal condition. EDA is usually considered to be the chelating agent or to function as a ligand to facilitate the growth of particles under hydrothermal reaction [36, 37]. However, phase transformation of iron oxide was observed when EDA was added into the alkaline solution. Thus, a special low-temperature route for the transformation of α-Fe2O3 to Fe3O4 was provided. The phase and shape variations with the addition of potassium hydroxide (KOH), EDA, and KOH and EDA were investigated and compared.


      Ferric nitrate (Fe(NO3)3 · 9H2O), 1 mmol, was dissolved in 10 ml of distilled water to form a transparent yellow solution. Next, three different mineralizing agents were added into the ferric solution. First is 5 ml of 10.67 M KOH aqueous solution. The solution was added dropwisely into the ferric solution. Second is 1 ml of EDA. The EDA was added gradually into the ferric solution. Third is the combination of KOH and EDA. The 10.67 M KOH solution, 5 ml, was added first followed by the addition of 1 ml of EDA. After adding these mineralizing agents, a brown Fe(OH)3 suspension was obtained. Then, these solutions were all stirred for 30 min before transferring the mixture into a Teflon-lined stainless steel autoclave (DuPont, Wilmington, DE, USA) of 40-ml capacity and followed by heat treatments at 200°C for 9 h. After that, the autoclave was cooled down to room temperature in air. The precipitates were collected by centrifugation, washed with deionized water and ethanol several times to remove organic and impurities, and finally dried in air at 80°C for 12 h.

      The as-synthesized powder was characterized by X-ray diffraction (XRD) with Cu-Kα radiation, field emission scanning electron microscopy (FE-SEM), transmission electron microscopy (TEM), and Raman spectroscopy. The magnetic properties were measured by a vibrating sample magnetometer (VSM) with a maximum magnetic field of 1.5 kOe.

      Results and discussion

      Figure 1 shows the iron oxide particles synthesized with three different reducing agents, KOH, EDA, and KOH/EDA, under a hydrothermal condition of 200°C for 9 h in the ferric solution. Figure 1a shows the α-Fe2O3 hexagonal plates which were obtained with the addition of KOH, and Figure 1b shows the α-Fe2O3 hexagonal bipyramid particles obtained when EDA was added into the system. Figure 1c shows the Fe3O4 polyhedral particles obtained with the addition of both KOH and EDA into the reaction system. (When NaOH substitutes for KOH, a similar reaction would occur.) The crystal structure of these iron oxide particles was analyzed by XRD and is shown in Figure 1d. The phase can be identified to be α-Fe2O3 when either KOH or EDA alone was added to the reaction system despite different morphologies. The diffraction peaks match the JCPDS card no. 33-0664 which is a rhombohedral structure with space group R 3 _ c http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq1_HTML.gif. The diffraction peaks obtained with the addition of both KOH and EDA into the reaction system correspond to the phase of Fe3O4, JCPDS card no. 19-0629, which is a face-centered cubic structure with space group Fd 3 _ m http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq2_HTML.gif. The characteristic reflections in the Fe3O4 phase and the γ-Fe2O3 phase are about the same [38]. Here diffraction of the (221), (210), and (213) planes for the γ-Fe2O3 phase does not exist. To further clarify the phase of polyhedral particles, the Raman spectra of α-Fe2O3 hexagonal plates and Fe3O4 polyhedral particles are shown in Figure 2. α-Fe2O3 here can be characterized by four strong peaks at around 225, 299, 412, and 613 cm-1 and two weak peaks around 247 and 497 cm-1. The peaks at 538 and 668 cm-1 were attributed to Fe3O4, while the peaks at 350, 500, and 700 cm-1 belonging to γ-Fe2O3 were not observed [39, 40]. The appearance of the Fe3O4 phase during reaction is a clear evidence that the valence change from Fe3+ to Fe2+ must occur due to the fact that Fe2+ ions occupy the octahedral sites of Fe3O4.
      Figure 1

      SEM images and corresponding XRD patterns of iron oxide particles. SEM images of iron oxide particles prepared with the addition of (a) 5 ml of 10.67 M KOH, (b) 1 ml of EDA, and (c) both 5 ml of 10.67 M KOH and 1 ml of EDA into the ferric solutions. (d) The corresponding XRD patterns of the iron oxide particles obtained for the cases of (a), (b), and (c).

      Figure 2

      Raman spectra of α-Fe 2 O 3 hexagonal plates and Fe 3 O 4 polyhedral particles.

      The α-Fe2O3 hexagonal plates have an average size of about 10 μm in edge length and about 500 nm in thickness. The average lateral size of the α-Fe2O3 particles with the shape of a hexagonal bipyramid is about 120 nm. The Fe3O4 polyhedral particles with mainly octahedral shape have an average lateral size in the range of 5 to 25 μm. The particles obtained from the reaction system with the addition of KOH and EDA alone have the same phase but different shapes. One would assume that the reaction system with the addition of both KOH and EDA would produce particles with maybe different shapes but still maintain the phase of α-Fe2O3. However, the results show that the particles that we obtained have a different phase, Fe3O4, and, surely, a different shape.

      The transmission electron microscopy images and the corresponding selected area electron diffraction (SAED) patterns of iron oxide particles are shown in Figure 3. The diffraction patterns of the particles confirmed the results of the XRD diffractions. In Figure 3b, the zone axis of the hexagonal plate is [0001] and the six directions normal to the edge are < 2 1 _ 1 _ 0 > http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq3_HTML.gif and its other five equivalent directions. In Figure 3d, the hexagonal bipyramid shows that the pyramid is pointed in the direction of <0001>. According to the literatures, the bipyramidal structure was enclosed by 10 1 _ 1 http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq4_HTML.gif crystal planes [41]. In Figure 3f, the Fe3O4 polyhedral particles which are composed of the pure magnetite phase and the diffraction spots are identified to be (202), 0 2 _ 2 http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq5_HTML.gif, and 2 _ 2 _ 0 http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq6_HTML.gif planes and their equivalent planes under an incident electron beam along 1 _ 11 http://static-content.springer.com/image/art%3A10.1186%2F1556-276X-9-230/MediaObjects/11671_2014_Article_2003_IEq7_HTML.gif.
      Figure 3

      TEM images and SAED patterns of α-Fe 2 O 3 hexagonal plates (a, b), α-Fe 2 O 3 hexagonal bipyramid (c, d), and Fe 3 O 4 polyhedral particles (e, f).

      To further understand the formation process of Fe3O4, the reaction systems with the addition of both KOH and EDA were hydrothermally synthesized at 200°C for different reaction times, as shown in Figure 4. Figure 4a shows that, after 2 h of growth, the main phase of the particles is α-Fe2O3 hexagonal plates. The edge of the hexagonal plate is not as straight as that obtained for the reaction system with KOH only. As the reaction time increased to 5 h, as shown in Figure 4b, small octahedron particles were observed and the original hexagonal plate started to dissolve and no longer maintained the hexagonal shape. As the reaction time continued to increase to 7 h, more polyhedron particles were observed with larger sizes and only a small amount of plate-like particles still existed, as shown in Figure 4c. At the reaction time of 9 h, the observed particles are mainly polyhedron ones, as shown in Figure 4d. The first observation in this sequence of experiment is that KOH can rapidly transform iron hydroxides to hematite. The second observed phenomenon is that the α-Fe2O3 hexagonal plates were dissolved to become irregular plates during the transformation process.
      Figure 4

      Mixture of α-Fe 2 O 3 and Fe 3 O 4 particles precipitated in the hydrothermal system at 200 °C at different times. (a) 2 h, (b) 5 h, (c) 7 h, and (d) 9 h.

      The result implied that phase transformation evolved in four steps: (1) the reaction systems rapidly transformed Fe(OH)3 or FeOOH to α-Fe2O3 hexagonal plates under the hydrothermal conditions, (2) the α-Fe2O3 hexagonal plates dissolved gradually, (3) the reduction process causes valence transition of Fe3+ to Fe2+, and (4) the Fe3O4 particles started to nucleate and then finally grew to form polyhedral particles.

      To further understand the role of NO3- ions on the phase transition process, the precursor of FeNO3 was substituted by FeCl3 with the same hydrothermal conditions. Two cases were investigated, one with the addition of KOH only and the other with the addition of both KOH and EDA under the same hydrothermal condition of 200°C for 9 h. Figure 5a shows that the α-Fe2O3 hexagonal plates were obtained when the reaction system consists of FeCl3 and KOH, while the phase transformation from α-Fe2O3 hexagonal plates to Fe3O4 polyhedral particles still occurred when the reaction system consists of FeCl3, KOH, and EDA, as shown in Figure 5b. The shape of the polyhedral particles is more irregular in this case. The XRD patterns, shown in Figure 4c, confirmed the related phases. Notice that the α-Fe2O3 plates were not completely reduced to Fe3O4 particles. Thus, NO3- ions are not directly involved in the reduction process of Fe3+ to Fe2+. However, the transformation process is faster with the presence of NO3- ions in the reaction system than that of Cl- ions.
      Figure 5

      SEM images and corresponding XRD patterns of iron oxide particles. SEM images of iron oxide particles formed with (a) FeCl3 + KOH and (b) FeCl3 + KOH + EDA. (c) The corresponding XRD patterns of iron oxide obtained for the cases of (a) and (b).

      We further explore the role that NO3- ions play on the phase transition. The pre-synthesized α-Fe2O3 hexagonal plates of 9 mg were added to the same KOH and EDA medium as above but with different amounts of HNO3 and heated to 200°C for 7 h. As shown in Figure 6, the results show that the phase transition rates were slow when the solution contained large and small amounts of HNO3; the optimal amount of HNO3 for phase transition is 0.19 ml. The slow phase transition rate observed for small amount of HNO3 may be attributed to the limiting dissolution of α-Fe2O3 which produced Fe3+ ion in the solution for further reduction to Fe2+. Thus, the rate of phase transformation is slow. At large amount of HNO3, the NO3- ions can be the oxidant in the reaction [29] and the pH value of the reaction system is changed toward a less basic solution. Hence, the reduction process can be again suppressed. Thus, there is a proper amount of HNO3 that induces the maximum rate for phase transformation.
      Figure 6

      The fraction of magnetite transformed with different amounts of HNO 3 . HNO3 was added to 9 mg of pre-synthesized α-Fe2O3, 5 ml of 10.67 M KOH, and 1 ml of EDA under hydrothermal process at 200°C for 7 h.

      A similar in situ reduction capability of EDA in neutral and basic solutions for the reduction of uranium from U6+ to U4+ has been reported by Jouffret et al. [42]. In our study, the phase transition process should be similar. The EDA maintains stable and chelates with Fe3+ ions that were released by α-Fe2O3 hexagonal plates upon dissolving, and the reduction of Fe3+ ions to Fe2+ ions occurred.

      Figure 7 shows the curve of transformed fraction of magnetite (α) as a function of reaction time. The fraction of α-Fe2O3 and Fe3O4 was determined by XRD measurement in conjunction with the Rietveld method. By using the Avrami equation, α = 1 - exp(-kt n ), where k is the reaction constant, t is the reaction time, and n is the exponent of reaction, we can fit, relatively well, the experiment data of the magnetite fraction obtained by hydrothermal treatment at 200°C for different times. The value of n is about 4 obtained in this case. From this curve, we can further investigate the kinetic behavior of phase transformation in the reaction condition in the future.
      Figure 7

      The fraction of magnetite transformed as a function of reaction time for Fe(NO 3 ) 3 , KOH, and EDA. Under hydrothermal reaction at 200°C.

      The magnetic properties of iron oxide particles followed the phase transition process from α-Fe2O3 hexagonal plates to Fe3O4 polyhedral particles, as shown in Figure 8. After a short reaction time of 2 h, the α-Fe2O3 hexagonal plates show weak ferromagnetic behaviors with a coercive force of 90 Oe at room temperature and the saturation magnetization is yet to reach the maximum in the range of the applied magnetic field, as shown in Figure 7a. Prolonging the reaction time to 5 ~ 7 h, the fraction of Fe3O4 polyhedral particles as well as the particle size of Fe3O4 increases gradually. As shown in Figure 7b,c, the values of saturation magnetization increase to 55 and 66 emu/g and the coercive forces decrease to 6.5 and 5.4 Oe for the reaction time of 5 and 7 h, respectively. Finally, the phase transition was completed at the reaction time of 9 h. The Fe3O4 polyhedral particles show strong ferromagnetic behaviors with the highest saturation magnetization of 80 emu/g and the lowest coercive force of 5 Oe, as shown in Figure 7d. The magnetic properties of α-Fe2O3 hexagonal plates and Fe3O4 polyhedral particles are similar to the previous reports [27, 43].
      Figure 8

      Magnetic properties of mixed α-Fe 2 O 3 and Fe 3 O 4 particles prepared by hydrothermally induced phase transformation at 200°C. (a) 2 h, (b) 5 h, (c) 7 h, and (d) 9 h.


      α-Fe2O3 nano/microhexagonal plates can be successfully reduced to octahedral Fe3O4 particles with EDA in an alkaline solution under a low-temperature hydrothermal process. In general, the transformation consists of four stages: (1) the formation of α-Fe2O3 hexagonal plates triggered by KOH, (2) the dissolution of the α-Fe2O3 hexagonal plates, (3) the reduction of Fe3+ to Fe2+, and (4) the nucleation and growth of new Fe3O4 polyhedral particles. The Avrami equation can be used to describe the transformation kinetics. As the phase transformation proceeded, the magnetic properties of the sample gradually transformed from weak ferromagnetic behaviors to strong ferromagnetic behaviors.

      Authors’ information

      JFL is a Ph.D. student at National Tsing Hua University. CJT holds a professor position at National Tsing Hua University.



      The authors acknowledge the support from the National Science Council through grant no. 101-2221-E-007-061-MY2.

      Authors’ Affiliations

      Department of Material Science and Engineering, National Tsing-Hua University


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      © Lu and Tsai; licensee Springer. 2014

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