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Observation of re-entrant spin reorientation in TbFe1−xMnxO3

Scientific Reports volume 6, Article number: 33448 (2016) | Download Citation

Abstract

We report a spin reorientation from Γ4(Gx, Ay, Fz) to Γ1(Ax, Gy, Cz) magnetic configuration near room temperature and a re-entrant transition from Γ1(Ax, Gy, Cz) to Γ4(Gx, Ay, Fz) at low temperature in TbFe1−xMnxO3 single crystals by performing both magnetization and neutron diffraction measurements. The Γ4 − Γ1 spin reorientation temperature can be enhanced to room temperature when x is around 0.5 ~ 0.6. These new transitions are distinct from the well-known Γ4 − Γ2 transition observed in TbFeO3, and the sinusoidal antiferromagnetism to complex spiral magnetism transition observed in multiferroic TbMnO3. We further study the evolution of magnetic entropy change (−ΔSM) versus Mn concentration to reveal the mechanism of the re-entrant spin reorientation behavior and the complex magnetic phase at low temperature. The variation of −ΔSM between a and c axes indicates the significant change of magnetocrystalline anisotropy energy in the TbFe1−xMnxO3 system. Furthermore, as Jahn-Teller inactive Fe3+ ions coexist with Jahn-Teller active Mn3+ ions, various anisotropy interactions, compete with each other, giving rise to a rich magnetic phase diagram. The large magnetocaloric effect reveals that the studied material could be a potential magnetic refrigerant. These findings expand our knowledge of spin reorientation phenomena and offer the alternative realization of spin-switching devices at room temperature in the rare-earth orthoferrites.

Introduction

The rare-earth orthoferrites RFeO3 (R = rare-earth elements) is a family of functional materials with large magnetoelectric (ME) coupling and optomagnetic properties1,2. Some of RFeO3 have been reported to be multiferroic materials with possible applications3,4,5. Furthermore, spin reorientation phase transition in such antiferromagnetic (AFM) insulators has attracted much attention since high-temperature Γ4(Gx, Ay, Fz) phase usually transforms to Γ2(Fx, Cy, Gz) at lower temperature3. Meanwhile, the rare-earth manganites RMnO3, aroused great interest in spintronics due to both colossal magnetoresistance (CMR) and magnetoelectric coupling effects6,7,8,9,10,11. The neutron diffraction experiments have revealed the existence of helical spin structure in RMnO3 (R = Tb, Dy) systems12,13,14,15 being the origin of their magnetoelectric coupling effect16,17,18,19.

The compounds of TbMnO3 and TbFeO3 both belong to the orthorhombic space group Pbnm with the same distorted perovskite structure. But they show distinct magnetic properties due to their totally different spin configurations. TbFeO3 has a canted AFM spin ordering caused by the Dzyaloshinskii-Moriya (DM) interaction5. Previous reports confirmed that most RFeO3 (R = Tb, Er, Sm, Tm, Yr, Sc, Nd, etc.) should undergo a spin reorientation transition from Γ4 to Γ23,5,20,21,22,23,24,25,26,27,28, as a second-order magnetic phase transition. Exceptionally, DyFeO3 exhibits an interesting Γ4 → Γ1(Ax, Gy, Cz) phase transition which completely annihilates weak magnetic moments observed in Γ4(Fz) or Γ2(Fx), along any crystallographic direction. This phenomenon has been observed in magnetization measurement, but not yet detected by neutron diffraction experiment due to the high absorption of Dy element. On the other hand, TbMnO3 manifests both magnetoelectric and magnetocaloric effect29,30, the latter is a key ingredient for high efficient magnetic refrigerant with large magnetic entropy change (−ΔSM). It was previously shown that the spiral spin structures of Mn3+ ions below 27 K lead to ferroelectricity29 and mutual controls of magnetism and electricity14,31. However, the spiral spin order is weak and can be easily destroyed by doping transition metals. Thus, although the parent compounds without doping are well investigated, the rich physics due to off-stoichiometry TbFe1−xMnxO3 is largely unexplored. It is our goal of present work to find out new magnetic phase and reveal the mechanism of new spin reorientation in TbFe1−xMnxO3 system, from which some remarkable behaviors expected to be found due to competitive magnetic phases that do not exist in both TbMnO3 and TbFeO3.

In this work, we synthesized a series of TbFe1−xMnxO3 and reported their special magnetic phase transitions by performing magnetization and neutron powder diffraction (NPD) measurements. We demonstrate that the phase transition of Γ4 → Γ1 → Γ4 exists in TbFe0.75Mn0.25O3 single crystal, rather than the common transition of Γ4 → Γ2 as observed in TbFeO3 and other orthoferrites. From a practical point of view, Γ4 → Γ1 (weak magnetic moment to zero net moment) transition may find use even with easily-obtained polycrystalline samples whereas we need to grow single crystals to observe Γ4 → Γ2 (weak magnetic moment along c to a direction) transition. The magnitude of the magnetocaloric effect is found to be large and strictly resembles the observed magnetic features. The evolution of entropy change versus Mn doping are presented and discussed with in the scenario of Mn substitution-induced anisotropic interaction.

Results

Magnetometry and neutron diffraction measurements

The x-ray diffraction patterns for the TbFe1−xMnxO3 with x = 0.25 are plotted in Fig. 1(a). The Rietveld refinement results show that the sample has a distorted orthorhombic perovskite structure (Pbnm) and no additional phases are identified. Figure 1(b) shows its temperature dependence of ZFC and FC magnetization curves with H = 100 Oe along the a (H || a), b (H || b) and c (H || c) directions, denoted as , , and . The total magnetic moment is parallel to c axis between 254 and 300 K. A sharp drop in occurs between 254 and 245 K, signaling the spin reorientation transition of Fe3+ ions23. When the temperature is between 16 and 254 K, the sample shows an antiferromagnetic state for H || c, while both and increase slowly for H || a and H || b with the decreasing temperature. This resembles the phase transition of Γ4 → Γ1 spin reorientation at TSR = 254 K. Thus, we speculate that the magnetic structure transforms from the canted antiferromagnetism with weak ferromagnetism along the c axis (Gx, Ay, Fz) to the major G-type antiferromagnetic vector along the b axis (Ax, Gy, Cz). In this case, there is no net magnetic moment along the c axis in the wide range of temperature between 16 and 254 K. Interestingly, as temperature decreases below 16 K, the magnetic moment along the c axis turns to be negative with a possible (Gx, Ay, Fz) configuration in negative magnetization state. The moment configuration speculated from the magnetometry is shown as the arrows in Fig. 1(b). The arrows show the evolution of magnetization arising from Tb (blue arrows) and Fe/Mn (orange arrows), respectively. The net moments of Tb and Fe tend to keep aligning along c-axis and parallel to the direction of applied field, which is responsible for the weak ferromagnetism above . Nevertheless, due to the d − f interactions of Fe/Mn and Tb ions, the larger net moment of Tb ions become antiparallel to those of Fe ions and the direction for applied field below in ZFC mode, leading to a negative magnetization state. However, in FC mode, both the net moments of Tb and Fe ions keep parallel to the direction of applied field, resulting in large net magnetization below .

Figure 1: Powder XRD refinement and magnetic phase transition of TbMn0.25Fe0.75O3.
Figure 1

(a) XRD patterns obtained by the ground crystal powders at room temperature. Inset is the optical-floating-zone grown single crystal on a grid of millimeter. (b) The temperature dependence of magnetization curves under H = 100 Oe. The shaded parts denote the magnetic phase transition and divarication of ZFC/FC. The arrows show the evolution of magnetization arising from Tb (blue) and Fe/Mn (orange).

To confirm our speculation on the nature of the intriguing spin reorientation transition phenomena, the NPD experiments were performed and the results are shown in Fig. 2(a–c) for T = 8, 40, and 300 K, respectively. All the structural Bragg peaks show no position shift or split, indicating the absence of structural phase transition at the different temperatures. Symmetry analysis was performed based on the crystal structure of TbFe1−xMnxO3 (x = 0.25), which is an orthorhombically-distorted perovskite structure with space group Pbnm. The lattice parameters for this crystal structure are a = 5.284 Å, b = 5.603 Å and c = 7.530 Å. For our orthoferrites, the k = 0 propagation vector was adopted as usual. According to the symmetry theory proposed by White32 and Bertaut20, Γ5 and Γ8 are incompatible with a net moment on the iron sites. Γ3 is not consistent with the observed strong antiferromagnetic coupling between nearest iron neighbors. So Γ1, Γ2 and Γ4 could be possible magnetic structure for this compound.

Figure 2
Figure 2

NPD patterns for TbFe1−xMnxO3 with x = 0.25 sample, obtained at (a) T = 8 K, (b) T = 40 K and (c) T = 300 K, respectively. The two lines of vertical bars present Bragg peaks for the crystal structures and the crystal with magnetic structures of Fe3+/Mn3+ respectively.

Then Rietveld refinements were performed to test these possibilities with the orthorhombic Pbnm structure. The results show that the data obtained at 8 and 300 K fit well with the magnetic structures of Γ4(Gx, Ay, Fz), and the data obtained at 40 K fit well with Γ1(Ax, Gy, Cz). The derived structures of Fe/Mn are schematically drawn in Fig. 3(a–c), respectively. Arrows of A-D represent four types of location of Fe(Mn) ions, and the corresponding refined magnetic moments along different crystallographic axes are given in supplemental material33. Figure 3(a) illustrates an orthorhombic perovskite with Fe/Mn having G-type AFM spin order along the a axis, A-type AFM spin order along the b axis, and F-type FM spin order along the c axis, consistent to the (GxAyFz) configuration at room temperature in Bertaut’s notation20. This type of commensurate spin order is observed to decline at  = 254 K and totally collapse at  = 245 K, resulting in a new antiferromagnetic phase with no net magnetization along any direction32. This intriguing magnetic phase configuration is found to be AxGyCz as shown in Fig. 3(b), instead of the common FxCyGz reported for most RFeO3 systems. This transition at is characterized by the relative change of the (011) intensity and the (101) magnetic Bragg peaks around |Q| = 1.4A−1 as shown in Fig. 2(b,c), implying that the moments of Fe3+ rotate from the a to b axis upon cooling as indicated in Fig. 3(a–c). With the further decrease of temperature, both () and increase gradually. It is noted that remains vanished till  = 16 K, then a sudden increase arises at . This sharp transition from Γ1 back to Γ4 is accomplished within 1 K and the results are confirmed by NPD. The ordering of Tb3+ has not been observed at T ≥ 8 K in our present measurement and further research at lower temperature is required. The at 254 K is believed to be driven by both Fe-Fe and Tb-Fe/Mn sub-lattice interactions, while at 16 K arises from the enhanced interactions of Tb-Fe/Mn sub-lattice5.

Figure 3: Evolution of magnetic phases for TbFe0.75Mn0.25O3.
Figure 3

The upper panels display (a) Γ4(Gx, Ay, Fz) phase at T = 300 K, (b) Γ1(Ax, Gy, Cz) phase at T = 40 K, and (c) Γ4(Gx, Ay, Fz) phase at T = 8 K. The lower panels illustrates the side view of the upper panels, respectively. Arrows of A-D represent four kinds of spin moments of Fe(Mn) ions.

Spin reorientation at

Since Γ4 configuration is characterized by the net moments along the c axis, the magnetic phase transition of Γ4 → Γ1 may undergo a transformation of the Fe3+ sublattice from weak ferromagnetism to complete antiferromagnetism upon the decreasing temperature. In order to reveal the relationship between Mn substitution and the changes in the anisotropy fields on the sublattices, a formula is developed by Holmes et al.23. Based on molecular field theory, the doping concentration dependence of obeys the following equation for x ≥ xc.

where k′ is a positive constant related to the second-order anisotropy fields in the b-a, b-c, c-a planes. xc characterizes a critical doping concentration from a hypothesis that at x = xc, the Γ4 → Γ1 spin reorientation first appears at T = 0 K. This formula reveals that Mn substitutions can be used to shift the Γ4 → Γ1 spin reorientation to be near or above room temperature. Figure 4 shows the experimental and fitting results for TbFe1−xMnxO3. Corresponding Eq. (1) with x = 0 ~ 0.6 and parameters xc ≈ 0.0080 and k′ = 0.0060 is adopted for this system. Since the Eq. (1) is only valid at low doping concentration, we can obtain good fitting up to x = 0.5. As shown in Fig. 4, could be taken as the onset point of the first spin reorientation transition, and can be enhanced to 299 K at x = 0.5. For x > 0.6, the spin reorientation transition phenomenon was not observed up to their Néel temperatures (TN). Moreover, the TN in Mn-rich TbFe1−xMnxO3 becomes much lower than that of the TbFeO3 (TN = 650 K), since Mn doping could weaken both the Tb3+-Fe3+ interaction and the Fe3+-Fe3+ interaction. In the high temperature Γ4 region of TbFe1−xMnxO3, the Tb3+-Fe3+ interaction is much stronger than that of Fe3+-Fe3+ interaction and the former one causes the parallel aligns between the moments of Tb3+ and Fe3+ to give rise to the net moments along c axis5. This scenario is supported from the magnetization behavior along c axis as indicated in Fig. 1(b). As a consequence, the substitution of Mn for Fe breaks the original Tb3+-Fe3+ interaction, leading to the shift of towards higher temeprature34.

Figure 4: as a function of x in TbFe1−xMnxO3 system.
Figure 4

The solid line is the fitting of Eq. (1).

Spin reorientation at

Compare with the Γ4 → Γ1 spin reorientation at , the Γ1 → Γ4 spin reorientation at presents more complex magnetic phase since the ordering degree and interaction between magnetic ions get larger and stronger at low temperature. We herein take TbFe0.75Mn0.25O3 as a representative of TbFe1−xMnxO3 system to discuss the characteristic of re-entrant Γ1 → Γ4 spin reorientation. Figure 5(a) shows a phase diagram of magnetic field versus temperature for x = 0.25, and the data points of crossover field Hcro were obtained from the isothermal M-H curves, in which Hcro is taken as the cross point between Ma-H and Mc-H curves (i.e. when Ma = Mc at a given temperature) from H = 0 kOe to 70 kOe. As the applied field increases, the M−T curves of the same system show dramatically different characteristics. The solid data points at the phase boundaries represent the second spin reorientation transition temperature for x = 0.25 sample, which divides the diagram into three magnetic phases, i.e., the first low temperature phase (LT1), the second low temperature phase (LT2), and intermediate temperature phase (IT). Both LT1 and LT2 phases are characterized as Γ4 type, and IT is of Γ1 type. LT1 presents a weak ferromagnetic phase with Γ4 type while LT2 regions show the negative magnetization behavior with Γ4 type. This phase diagram illustrates the phase transition Γ1 → Γ4 can be modified by the external field at low temperature, resulting in rich variation of magnetocrystalline anisotropy.

Figure 5: The phase diagram of magnetization vectors of TbFe1−xMnxO3 (x = 0.25) by tuning the applied magnetic field and temperature.
Figure 5

LT1: low temperature phase-1, LT2: low temperature phase-2, IT: intermediate temperature phase.

Discussion

Several factors may affect the spin reorientation transition phenomena: single ion anisotropy, DM interaction, exchange interaction, and magnetic anisotropy35. For a rare-earth ion, 4f orbital electrons make it special in bonding and the compounds have large single ion anisotropy. Consequently, the giant magnetocrystalline anisotropy and sharp spin reorientation can be attributed to the single ion anisotropy of Tb3+ with large angular momentum. For a spin-canted system36,37,38,39, a ubiquitous antisymmetric interaction D (S1 × S2) exists, which is linear with respect to the spin-orbit coupling and exchange interaction. The magnitude of D can be expressed roughly as D ≈ (Δg)/(g)Jsuper, where g is the gyromagnetic ratio, Δg is its deviation from the value for a free electron, and Jsuper is the strength of superexchange interaction. According to the magnetocaloric and NPD data, we can regard the magnetic entropy change between the a and c axes as a measurement of magnetocrystalline anisotropy energy and analyze the superexchange interactions in our TbFe1−xMnxO3 system.

In order to illustrate the variation of magnetocrystalline anisotropy energy versus Mn doping concentration, we estimate that the magnetic entropy change (−ΔSM, where ) between the a and c axes in TbFe1−xMnxO3 single crystals. According to Maxwell’s relation40,41, the magnetic entropy change in a thermodynamic process can be estimated using the following equation

We take the ΔT = 1 K (or no more than 5 K at higher temperature) and ΔH = 1 kOe and the computed results are illustrated in Fig. 6(a–f). From Eq. (2), the magnetic entropy change is a function of both temperature and magnetic field. Therefore, by changing temperature and magnetic field, the direction of magnetization vector will rotate due to the magnetocrystalline anisotropy field, and the distribution of anisotropy energy will also vary. Hereafter, we denote the magnetocrystalline anisotropy energy as Eani. It is noted that the −ΔSM value decreases from x = 0 to x = 0.5 and then increases to x = 1, suggesting a similar tendency for the Eani. The evolution of −ΔSM versus doping concentration x implies that the superexchange interaction weakens along the c axis while enhances along the a or b axes for 0 ≤ x ≤ 0.5, and the reversed case holds for 0.5 ≤ x ≤ 1.

Figure 6: The distribution of magnetic entropy change as a function of the temperature and Mn concentration x under different applied fields.
Figure 6

(a) H = 3 kOe, (b) H = 10 kOe, (c) H = 20 kOe, (d) H = 30 kOe, (e) H = 50 kOe, (f ) H = 70 kOe.

In TbFe0.75Mn0.25O3, the hard axis is along the c direction, and the easy magnetization vector is along a direction as shown in Fig. 6. This contour plot of −ΔSM reveals the state of Eani, which may affect both the magnitude and the direction of magnetization vectors. Furthermore, it is noted that the magnitude of net magnetic moment is usually small but its direction is often a decisive factor when considering the exchange coupling interactions in a system42. According to our NPD experiment, the Tb3+ ions are in paramagnetic state at T ≥ 8 K. Therefore, the Tb-Fe(Mn) interactions should be very weak so that they can hardly be influenced by the crystal field. As the applied field increases, ZFC magnetizations in Γ4 phase become increasing larger, as shown by the ZFC-FC convergence near the Γ4−Γ1 transition (Fig. 5b–d). Thus, the effect of the external field plays a determining role on Γ4−Γ1 transition which to be explored in future.

According to the NPD experimental results15,29, the evolution of spin configurations versus doping content x is schematically illustrated in the upper panels of Fig. 7(a–c). In the lower panels of Fig. 7(e,f), the spin glass (SG) transition TSG occurs at 16 and 6.5 K along the c axis under H = 100 Oe in both TbFe0.75Mn0.25O3 and TbMnO3 single crystals, respectively. However, the SG state is not detected along any axis down to 1.9 K in TbFeO3 single crystal from Fig. 7(d), nor a and b axes in TbFe0.75Mn0.25O3 and TbMnO3 single crystals. The observation of SG behavior is attributed to the competition between AFM and FM component, leading to a spin frustration in Fig. 7(e,f). The M-O-M bond angle (M = Fe or Mn), namely, superexchange interaction angle, is usually reduced from 180° due to the cooperative octahedral rotations in the orthorhombic perovskites. In RMO3 systems43, the easy magnetization axis may rotate below TN because of the coupling between magnetic moments of rare earth R ions and the spin of transition metal M ions. As the major controlling factor of the superexchange interaction, the coupling of M-O-M is much stronger than that of R-O-M, which should be neglected. In TbFe1−xMnxO3 system, the Fe-O-Fe interaction can be partially replaced by Fe-O-Mn upon Mn3+ doping. In Fig. 7(b,c), the spin frustration along c axis causes the anisotropic superexchange interaction decreasing along the c axis by Mn substitution, which means the entropy change between the a and c axis gets weaker as x increases in a Fe-rich TbFe1−xMnxO3 system. The mechanism of SG phenomena is as follows.

Figure 7: The spin configurations and spin glass state in TbFe1−xMnxO3 system.
Figure 7

(a) x = 0, no SG behavior down to 1.9 K, (b) x = 0.25, SG transition at 16 K, (c) x = 1.0, SG transition at 6.5 K. The sketches in upper panels show the variation of spin configurations in the bc-plane versus x and the lower panels show the M-T curves along the c axis under H = 100 Oe.

Since the ionic radius of Fe3+ is equal to Mn3+ in high spin state (Fe3+: S = 5/2, 5.9 μB/at., r = 0.645 Å and Mn3+: S = 2, 4.9 μB/at., r = 0.645 Å), the crystal distortion caused by ionic radius difference can be ignored. It should be pointed out that the hybridization between inter-site t and e orbitals is orthogonal for a 180° M-O-M chemical bonding. The sketches of Fig. 8(a–c) describe the different effects of Mn3+ and Fe3+ ions on the orbital hybridization. According to Goodenough-Kanamori rule44, the superexchange interaction between two adjacent transition-metal ions is delivered by a virtual charge transfer. The Fe3+ and Mn3+ ions present different configurations for the outer shell electrons, i.e., t3e2 for Fe3+ and t3e1 for Mn3+, respectively. In RFeO3, five outer shell electrons of Fe3+ ions lead to half-filled eg (σ-bond component) and t2g (π-bond component) orbitals. Therefore, the superexchange interactions between the two Fe3+ ions only result in an AFM coupling, in accordance to Hund’s rules. For Mn3+ ions, there are three kinds of coupling, i.e., t3-O-t3, e1-O-e1 and t3-O-e1. The superexchange interactions over the half-filed t3-O-t3 induce an AFM coupling. Nevertheless, the hybridization between t3-O-e1 and e1-O-e1 might provide an FM coupling in the system, which experimentally confirms that the spiral spin states in TbMnO3 originate from spin frustration29. The above argument can help us explain the SG phenomena in Fig. 7(b,c).

Figure 8
Figure 8

Schematic diagrams of the hybridization effect on the virtual charge transfer for (a) Fe-Fe, (b) Fe-Mn, (c) Mn-Mn, based on Goodenough-Kanamori rules in TbFe1−xMnxO3 system. The occupied state for electrons implicates that Mn substitution promotes the FM component. (d) The θ becomes smaller when Fe doping content increases, in accompany with the weaker lattice distortion.

Now we look at the Mn-rich TbFe1−xMnxO3 system. As illustrated in Fig. 8(b,c), the Mn substitution gives rise to the FM component in TbFe1−xMnxO3 system with two consequences. One is the appearance of spin-glass state in Fig. 7(b,c), and the other one is the variation of anisotropic −ΔSM. In TbFe1−xMnxO3 (x > 0.5), Mn3+ substitution can induce more FM component and lead to a stronger lattice distortion in the system. These factors induce a spin frustration state and result in the reduction of superexchange interaction. In RMnO3 system, the occupied eg orbital wavefunction of Mn is given by Eq. (3)

where θ is the respective orbital component (Fig. 8(d)). The ground state of the system is given by any normalized linear combination of the two eg orbitals in Eq. (3). In TbMnO3, the Jahn-Teller distortion of MnO6 octahedral is a mode of elongating along one axis but shrinking in the other two axes. Since the rare-earth ferrites belong to Jahn-Teller inactive system, θ becomes smaller with doping from x = 1 to 0.5, and the shape of wavefunction |ϕ> will be stretched. Therefore, the distance of Mn(Fe)-Mn(Fe) along the c axis between the Mn(Fe)O6 octahedra should be longer than that in TbMnO3. Thus the superexchange interaction in TbFe1−xMnxO3 is suppressed along the c axis. Additionally, the application of external magnetic field can increase the lattice distortion and enhance the DM interaction45,46. The above discussions can account for the variation of −ΔSM for 0.5 ≤ x ≤ 1.

In summary, we observed a re-entrant spin reorientation of type Γ4 → Γ1 → Γ4 in TbFe0.75Mn0.25O3 perovskite system. Through neutron powder diffraction and magnetization measurements, we have observed the recurrent magnetic phase transitions at 254 and 16 K. With Mn doping, the spin configurations can be modified and the spin glass state emerges due to the competition between AFM and FM components. Furthermore, the first spin reorientation temperature increases from 8.5 K for x = 0 to 299 K for x = 0.5 TbFe1−xMnxO3 sample, which might be useful for developing spin-switching devices. We have found a rich phase diagram of magnetization by tuning the applied magnetic field and temperature. In the framework of Goodenough-Kanamori rule, we analyze the evolution of −ΔSM versus Mn doping to reveal the unusual spin reorientation and abundant magnetic phase diagram. It is found that the −ΔSM decreases for 0 ≤ x ≤ 0.5 and increases for 0.5 ≤ x ≤ 1. The evolution of −ΔSM is attributed to the change of anisotropic interactions tuned by Mn doping concentration. Furthermore, in an ongoing project we have discovered similar results in Mn doped HoFeO3 and DyFeO3, with Mn dopants in RFeO3 triggering a rare phase transition from normal Γ4 → Γ2 to re-entrant Γ4 → Γ1 → Γ4 spin reorientation.

Methods

A series of Mn doped terbium orthoferrites TbFe1−xMnxO3 (x = 0, 0.10, 0.25, 0.40, 0.50, 0.60, 0.70, 0.80, 0.90, 1) polycrystalline samples were first synthesized by traditional solid state reaction method. Single crystals of x = 0, 0.10, 0.25 and 1 were then grown by using a four-mirror optical floating-zone furnace (FZ-T-10000-H-VI-P-SH, Crystal System Corp.). The phase purity, crystal quality, and crystallographic orientation were checked by powder X-ray diffraction (XRD) and back-reflection Laue XRD experiment, respectively. Magnetization measurements were performed on vibrating sample magnetometer (VSM) attached to a physical property measurement system (PPMS-9), and both zero-field-cooling (ZFC) and field-cooling (FC) modes were used. The NPD experiments at 8, 40, and 300 K were carried out on the thermal triple-axis spectrometer SV30 located at China Advanced Research Reactor (CARR) in China Institute of Atomic Energy, and the neutron powder diffractor at the Institute of Nuclear Physics and Chemistry, China Academic of Engineering Physics. The structural data analyses of XRD and NPD were performed by FullProf program using Rietveld method47, and the magnetic symmetry analysis was performed with BasIReps.

Additional Information

How to cite this article: Fang, Y. et al. Observation of re-entrant spin reorientation in TbFe1−xMnxO3. Sci. Rep. 6, 33448; doi: 10.1038/srep33448 (2016).

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Acknowledgements

This work was supported by the National Natural Science Foundation of China (NSFC, Grants No. 11574194,51372149), the National Key Basic Research Program of China (Grant No. 2015CB921600), the Eastern Scholar Program and the Shuguang Program (Grant No. 12SG34) from the Shanghai Municipal Education Commission, Shanghai Institute of Materials Genome from the Shanghai Municipal Science and Technology Commission.

Author information

Affiliations

  1. Materials Genome Institute, Shanghai University, Shanghai 200444, China

    • Yifei Fang
    • , Fei Chen
    • , Shixun Cao
    •  & Jincang Zhang
  2. Department of Physic, Shanghai University, Shanghai 200444, China

    • Yifei Fang
    • , Ya Yang
    • , Jian Kang
    • , Venkatesh Chandragiri
    • , Yiming Cao
    • , Shixun Cao
    • , Wei Ren
    •  & Jincang Zhang
  3. Neutron Scattering Laboratory, China Institute of Atomic Energy, Beijing 102413, China

    • Xinzhi Liu
    • , Lijie Hao
    • , Yuntao Liu
    •  & Dongfeng Chen
  4. Insititute of Nuclear Physics and Chemistry, China Academy of Engineering Physics, Mianyang 621999, China

    • Xiping Chen
    • , Lei Xie
    •  & Guangai Sun
  5. ANSTO, Kirrawee Dc, NSW 2232, Australia

    • Chin-Wei Wang
  6. Max Planck Institute for Solid State Research, Heisenbergstraße 1, D-70569 Stuttgart, Germany

    • Chengtian Lin

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Contributions

Y.F. and J.Z. conceived the project. Single crystal samples, characterizations and magnetometry measurements were grown and performed by Y.F., NPD data were taken by X.L., Y.F., L.H., X.C., L.X., G.S., Y.L., D.C. and C.-W.W., Y.F., Y.Y., X.L., J.K., V.C., Y.C. and S.C. have contributed to analyze the results, and Y.F., W.R., C.L., V.C., F.C. and J.Z. wrote the manuscript. All authors reviewed the manuscript.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Wei Ren or Jincang Zhang.

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https://doi.org/10.1038/srep33448

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