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Tuning the Weak Ferromagnetic States in Dysprosium Orthoferrite

Scientific Reports volume 6, Article number: 37529 (2016) | Download Citation

Abstract

RFeO3 orthoferrites, where R is a rare-earth ion of the lanthanide series, are attracting attention mostly because of their promising fast spin dynamics. The magnetic properties of these materials seem to crucially depend on whether the magnetizations of the R and Fe ions’ weak ferromagnetic (WFM) components are parallel or antiparallel to each other. Here, we report an extensive investigation of a high-quality DyFeO3 single crystal in which the induced Dy3+ magnetization (FDy) has a natural tendency to be antiparallel to Fe3+ sublattice magnetization (FFe) within a large temperature window. Moreover, we find that specific variations of temperature and applied magnetic fields allow us to make FDy parallel to FFe, or force a spin-flip transition in FFe, among other effects. We found three different magnetic states that respond to temperature and magnetic fields, i.e. linear versus constant or, alternatively, presenting either behavior depending on the history of the sample. An original magnetic field-versus-temperature phase diagram is constructed to indicate the region of stability of the different magnetic phases, and to reveal the precise conditions yielding sudden spin switching and reversals. Knowledge of such a phase diagram is of potential importance to applications in spintronics and magnetic devices.

Introduction

Dysprosium orthoferrite DyFeO3 (DFO) has been investigated since the 1960s for its particular magnetic structure and properties1. Recently, DFO has drawn renewed attention because of, e.g., its laser or terahertz wave induced spin dynamics2,3,4,5,6,7,8, magnetic-field- or uniaxial-stress-induced multiferroic state9,10,11, and Mossbauer spectrum12. DFO, like the other rare-earth orthoferrites, is a distorted perovskite crystallizing in an orthorhombic lattice with the Pbnm space group. There are two magnetic sublattices in DFO, namely those associated with Fe- and Dy-ions, which provide three different types of magnetic interactions, namely, Fe3+- Fe3+, Fe3+- Dy3+, and Dy3+- Dy3+ couplings. The Fe3+- Fe3+ exchange energy determines the predominant magnetic ordering of the iron sublattice below the first Néel temperature (TN1) of about 650 K, that is, a G-type antiferromagnetic structure in which nearest-neighboring irons have anti-parallel spins. In addition, because of a specific Dzyaloshinskii-Moriya (DM) interaction mediated by the tilting of the oxygen octaheda13, the Fe spins are not perfectly collinear but, instead, are slightly canted with respect to one another. Indeed, in the so-called Γ4 configuration of DFO, which is the most stable magnetic state for the temperature region ranging from TN1 down to 50 K, the G-type antiferromagnetic vector lies along the a-axis, and the aforementioned canting provides a weak ferromagnetic component (overt canting) along the c-axis, as well as a weak C-type antiferromagnetic component (hidden canting) along the b-axis1,14. At 50 K, a spin reorientation (SR) transition to a so-called Γ1 state occurs15, in which the G-type antiferromagnetic vector now points along b, the overt canting vanishes, and two new hidden cantings of A and C types appear along the a and c-axes, respectively1,14,16.

The antiferromagnetic transition temperature (TN2) of the Dy3+ sublattice is two order of magnitudes lower than TN1, namely about 4.5 K. The resulting Dy3+ spin configuration was reported to be GxAy in a previous study on DyAlO317. Moreover, when a magnetic field is applied along the c-axis in this particular state, the system exhibits a magnetic-field-induced phase transition and an electric polarization appears18. Furthermore, both weak ferromagnetism and ferroelectricity are also obtained when applying stress along the [110] direction to the low-temperature state with both Dy and Fe spins ordered.

A specific interaction between Fe and Dy neighboring ions can also exist in the Γ4(Gx, Ay, Fz) state, and is of the utmost importance since it can result in a net magnetization of Dy3+ ions being either parallel or antiparallel to the net Fe3+ sublattice moment aligned along the c-axis19,20. Previous magnetizing studies of the Γ4 phase of DFO single crystals reported that the magnetizations of Dy and Fe sublattices are parallel to each other1,21. However, these studies were carried out with a relative large applied field (about 500 Oe)21, which may force both the overt canting component of Fe3+ sublattice, FFe, and net Dy3+ moment component, FDy, to arrange along the field’s direction. Therefore, it is not clear whether such experiments shed light on the intrinsic, zero-field spin configurations and magnetizing behavior of the material.

In order to uncover the basic spin configuration, in general, and reveal the relative arrangement of FFe and FDy in the Γ4 phase for different fields and temperatures, in particular, we employ here small as well as large applied fields at various temperatures. The present work revisits the pioneering studies of refs 1 and 21, as our results suggest that that FFe and FDy tend to align antiparallel to each other, and not parallel as previously proposed. It is also discovered that the application of magnetic fields can result in a magnetic transition, driving FDy to align parallel to FFe. Importantly, an original temperature-versus-magnetic field phase diagram within the Γ4 phase is further provided here, with this diagram exhibiting three different regions, each possessing its own distinct behavior for the dependence of the weak magnetization as a function of the magnetic field (i.e., linear versus constant or, alternatively, presenting either behavior depending on the history of the sample). Our results also reveal the precise conditions required to induce the reversal of the magnetization of the Dy sublattice and the flip of the Fe spins. All these (previously overlooked) possibilities for controlling the magnetic state and response of DyFeO3 render a highly tunable material, with potential important applications in the context of spintronic devices.

Results

Crystal Growth, Sample Preparation and Basic Characterization

Figure 1(a) shows the DFO single crystal grown in floating air, with a 6 mm diameter and a 85 mm length. The as-grown crystal rod presents a pair of parallel cleavage planes along the growth direction, whose normal vector is confirmed to be the b-axis by Laue camera. Further orientation results are displayed in Fig. 1(b) by means of a sketch, indicating that the c-axis is slightly canted (~13°) from the growth direction. We then cut this crystal rod into a cuboid with a length of 2.4 mm, 2.6 mm and 1.4 mm along the a, b, and c axes, respectively. Figure 1(c–e) shows the X-ray Diffraction (XRD) patterns, which allow to identify characteristic peaks for each axis. Note that the insets of Fig. 1(c–e) are Laue photographs for each crystallography axis corresponding to the XRD peaks. Moreover, Fig. 1(f–h) show the XRD rocking curves for the (200), (020), and (004) peaks, indicating that the full-width at half-maximum (FWHM) is 0.11, 0.05 and 0.08 degree, respectively. Both the XRD and Laue data demonstrate that a high quality DFO single crystal sample was successfully grown under our conditions. Moreover, magnetic properties are displayed in Fig. 1(i–k), and measured via three different procedures – i.e., ZFCH, FCC and FCH–all using an applied field of 100 Oe (see Methods to describe these procedures).

Figure 1: Characteristics and properties of the grown DyFeO3 (DFO) single crystal.
Figure 1

(a) Photograph of it; (b) Sketch to display its axes with respect to crystallographic directions; (c–e) Its X-ray diffraction (XRD) patterns along the a-, b-, and c-axis, respectively, with the inset displaying the Laue photographs; (f–h) Its XRD rocking curves corresponding to (200), (020), and (004) peaks, respectively; (i–k) a-, b- and c-axis magnetization, respectively, as a function of temperature, for ZFCH, FCC and FCH (see text) measurements with an applied field of 100 Oe.

As shown in Fig. 1(i,j), the a- and b-axis magnetizations, whose ZFCH, FCC and FCH curves all coincide, show a rapid upturn below 50 K, which corresponds to the SR transition from Γ4 to Γ1. All these magnetizations also exhibit a sharp decrease at TN2 ~ 4.5 K, due to the formation of the antiferromagnetic (GxAy) state of the Dy spins. The magnetization along the c-axis is different from the a- and b-axis magnetizations. For instance, a large c-axis magnetization is present at the highest studied temperatures, due to the weak ferromagnetism (WFM) of the Fe3+ sublattice, and an abrupt decrease occurs at 50 K as a result of the SR transition. Further cooling within the Γ1 state results in a rather negligible c-axis magnetization value. It is important to realize that Fig. 1k shows that our measured c-axis magnetization in the ZFCH procedure (which coincides with the FCH curve) is approximately constant between 50 K and 200 K, which contrasts with previous studies reporting a gradually decrease with temperature above the SR transition11,21. This difference is likely due to the application of relatively large magnetic fields (well above our used value of 100 Oe) in these previous works. Moreover, another new result is found here, namely, the FCC curve is separated from the two heating curves (ZFCH and FCH); such a behavior is similar to the one observed for the a-axis magnetization of dysprosium samarium orthoferrite single crystals14.

The Relative Orientation between Fe and Dy Sublattice Moments

According to previous studies in rare-earth orthoferrites14, the nearly temperature-independent behavior of the ZFCH magnetization curve of Fig. 1k between 50 K and 200 K would be representative of an antiparallel coupling between the Fe3+ sublattice overt canting (FFe) and its induced rare-earth net moment. On the other hand, the sharp increase of the FCC magnetization of Fig. 1k when cooling the system from 200 K to 65 K is characteristic of a net Dy3+ moment (FDy) being parallel, rather than antiparallel, to FFe, as also consistent with previous studies where relatively large fields were applied1,11,21. The fact that the FCC magnetization exhibits a sudden jump at 65 K, which results in the convergence with the two curves obtained upon heating (ZFCH and FCH), can therefore be thought of as signaling a parallel-to-antiparallel (PA) transition. In other words, the WFM of the Dy sublattice evolves from being parallel to becoming antiparallel to the WFM associated with the Fe ions. Furthermore, Fig. 2(a–e) explore the effect of the magnitude of the applied magnetic field on the c-axis magnetization in the FCC and FCH processes. One can see that there is no PA transition for a field of 50 Oe, as evidenced by the fact that the FCC curve is very similar to the ZFCH one for any investigated temperature. FDy therefore appears to be antiparallel to FFe both upon cooling and heating for that small field, thus suggesting that the antiparallel magnetic configuration is the most stable one for the Γ4 phase of DFO at zero field. On the other hand, a sudden departure of the FCC curves with respect to ZFCH curve does occur for magnetic fields of 75 Oe and 100 Oe; further, the temperature of the magnetization jump that we interpret as a PA transition gets reduced for increasing the magnetic field (e.g., we get 65 K for 75 Oe, and 57 K for 100 Oe). Another interesting feature is that, for an applied field of 200 Oe, the FCH curve does not display any plateau within the stability range of the Γ4 phase, but rather follows closely the FCC curve for any temperature. Such a result indicates that, for that larger field, FDy is always parallel to FFe both in the cooling and heating processes above the SR critical temperature.

Figure 2: Temperature dependence of the c-axis magnetization for a DFO sample that is initially demagnetized at 500 °C.
Figure 2

(a) FCC and FCH measurements (solid lines) under different magnetic fields of 50, 75, 100 and 200 Oe, with the star symbols reporting the values of FFe + FDy and FFe − FDy obtained from Fig. 4. Zoom-in magnetization curves under the magnetic fields of 50, 75, 100 and 200 Oe are shown in (b–e), respectively, with the arrows indicating the spin reorientation (SR) and the parallel-antiparallel (PA) transition.

To ratify the naturally antiparallel alignment of FFe and FDy, we conducted another experiment whose results are reported in Fig. 3(a). The demagnetized (please see the details in Methods) DFO was then placed into the chamber, cooling it down to 4 K and then heating it up. The magnetization measurements were performed both during the cooling (Zero-Field Cooling Measurement) and heating (Zero-Field Heating Measurement) processes. As shown in Fig. 3(a), upon cooling we measure a negative c-axis magnetization within the stability range of the Γ4 phase; for example, a value of 2 × 10−3μB/f.u. is found at the highest investigated temperature of 300 K. This magnetization is about thirty times smaller than the one reported in Fig. 1k (which is close to 6 × 10−2μB/f.u.). Such small negative value arises from the fact that (i) our thermal demagnetization process favors a vanishing FFe (as a result of magnetic moments of iron ions being randomly oriented up and down, as schematized in Fig. 3(c), which is a direct consequence of the existence of different antiferromagnetic domains with differently oriented FFe moments, but (ii) the downward geomagnetic field slightly magnetizes the Fe sublattice, as modeled in Fig. 3(b)). When cooling the system from 300 K to 210 K, the total magnetization remains small and negative but slightly increases in magnitude to reach 2.5 × 10−3 μB/f.u., which we attribute to the increasing ordering of the Fe spins. Further cooling below 210 K and down to 50 K results in a total magnetization decreasing in strength until becoming rather small (about 1 × 10−4 μB/f.u.). This stationary point at about 210 K likely indicates the appearance of FDy, which is induced by, and antiparallel to, FFe. This net moment of Dy ions, FDy, then grows as the temperature is reduced down to 50 K, which explains the concomitant decrease of the magnitude of the total magnetization. The spin reorientation then happens, which yields an almost complete annihilation of the total magnetization below 50 K. Interestingly, Fig. 3(a) further shows that the heating process significantly differs from the cooling one, as evidenced by the fact that the total magnetization upon heating is now positive after the Γ1 to Γ4 SR transition has occurred.

Figure 3: Magnetic characteristics for a DFO sample that is initially demagnetized at 500 °C.
Figure 3

(a) Temperature behavior of the c-axis magnetization as measured in a quasi-zero-field cooling and heating processes. (b) Representation of the spin structure of DFO in the Γ4 configuration; small arrows at the Dy cations indicate the weak magnetization induced by the interaction with the Fe spins. (c) Schematization of different proposed magnetic states.

Let us now discuss in more detail the magnetic response of DFO in the Γ4 phase, to see whether it offers additional hints on the spin structure and interplay between the Fe and Dy sublattices. Figure 4(a–f) display the magnetization hysteresis loops (MH curves) measured at several temperatures in the relevant range. DFO is demagnetized before conducting each MH measurement, in order to get a nearly vanishing initial magnetization. We find that the magnetization increases when applying a magnetic field (starting from the M ~ H ~ 0 point) until reaching a plateau for the largest (positive) applied fields during the MH process. The existence of such a plateau shows that the WFM component of the total magnetization is saturated for these relatively large fields. Note that these saturated values are also consistent with the MT curves reported in Fig. 2(e) for the FCC and FCH measurements corresponding to the application of fields up to 200 Oe.

Figure 4: Magnetic properties of a grown DFO sample that is initially demagnetized at each studied temperature.
Figure 4

(a–f) Magnetization-versus-magnetic field hysteresis loops measured at temperatures of 52, 100, 150, 200, 250 and 300 K, respectively. Violet arrows indicate the followed path in terms of the variation of the applied magnetic field, and the inset of Panel (f) zooms in the region extending from 0 to 50 Oe. (g) The initial part of these loops for the different investigated temperatures. The inset of (g) shows the decomposition discussed in the text of this initial part at 52 K, in order to extract FFe and FDy. (h) The temperature behavior of the resulting FFe and FDy.

In Fig. 4(g) we show the initial part of the MH curves (i.e., starting from a demagnetized sample and progressively increasing the field’s magnitude) for all studied temperatures. These results indicate that the total magnetization first increases linearly with the field, and then departs from linearity at a certain field magnitude. We can conjecture that the response in the first segment is dominated by the relatively large FFe canting, while the relatively small FDy is probably still pointing along the opposite direction. Note that, in this regime, FDy will be subject to two competing forces that both scale linearly with the applied magnetic field: on one hand we have the direct action of the applied field, which drives both FFe and FDy pointing along the field’s direction; on the other hand we have the anti-parallel coupling with FFe, which itself grows linearly with the field. As the applied field grows, FFe eventually saturates, and FDy progressively aligns parallel to the applied field (and to FFe) in the second segment of the response.

Following this picture, we quantitatively analyzed the results of Fig. 4(g), in the following way: we first draw a (purple) line fitting the data at smaller fields and then another line fitting data at higher fields (see the inset of Fig. 4(g) for the case of 52 K). The magnetization value associated with the intersection of these two lines is interpreted as being the difference between the saturated values of FFe and FDy, while the plateau of the MT curves in Fig. 4(g) corresponds to the sum of the saturated values of FFe and FDy. Thus, for instance, the inset of Fig. 4(g) shows that the saturated values of FFe and FDy at 52 K are 0.133 μB/f.u. and 0.015 μB/f.u., respectively. Such a procedure therefore allows us to extract the saturated values of FFe and FDy at all investigated temperatures, and the corresponding results are shown in Fig. 4(h). It is interesting to realize that FDy vanishes above 200 K, as consistent with the results in Figs 1k, 2c,d and 3a. Moreover, the values of FFe + FDy and FFe − FDy thus obtained are also reported in Fig. 2(a) by means of symbols; we find that the total saturated WFM values are consistent with the FCC MT curves for fields above 75 Oe, while the obtained difference of saturated moments agree well with data of the FCH MT curves for fields close to 100 Oe field. Note that the value of 100 Oe roughly corresponds to the field at which the slope of the MH curve changes (see inset in Fig. 4(g)), supporting the validity of our analysis.

Mapping of the WFM States

Let us now focus on the hysteresis characteristics of DFO in the Γ4 phase, trying to understand the origin of the various behaviors obtained. For the purpose of this discussion, it is convenient to introduce what we denote as the standard MH hysteresis loops in Fig. 4(a–f), that is, the loops one obtains by starting from the maximum positive field of 250 Oe, then continuously decreasing this field down to a negative field of −250 Oe, and finally continuously varying again this field from the aforementioned negative to positive maximum fields to complete the cycle. Interestingly, and as shown in Fig. 4, these standard loops adopt a square-like form for temperatures above 150 K. In particular, once the plateau is reached from the initial state, the MH curves never display a linear behavior again. In contrast, at temperatures below 150 K, we find that it is impossible to obtain the square-loop behavior: by application of a magnetic field we reach a plateau as in the cases above 150 K; yet, when the field decreases and eventually changes sign, at some point the material falls back (abruptly in some cases, like at 100 K in Fig. 4(b)) into a state with a linear MH characteristic, and the transition to the state with large but opposite magnetization is ultimately gradual.

To rationalize these behaviors, it is useful to distinguish three regions in the field-temperature phase diagram of the material, as shown in Fig. 5(a): We have regions in which the material always presents a flat MH characteristic, a situation that we denote “hard WFM” state. The boundary of this region is given by the temperature-dependent magnetic field values at which the MH plateau is reached (see Fig. 4); this boundary is marked by red lines and squares in Fig. 5(a). Then, we have a region of the phase diagram in which the material can present either a square-like MH curve or a linear one, depending on the history of the sample. This is what we call the “history-dependent WFM” region in Fig. 5(a). Finally, there is a region of the phase diagram within which the measured MH curves are always linear, independently of the history of the sample; this is what we call “soft WFM” region in Fig. 5(a). Such “soft WFM” MH behavior can only be found in low temperature region. Indeed, as can be seen in Fig. 4 and is reflected in the phase diagram of Fig. 5(a), for high enough temperatures (roughly above 90 K) we always obtain square MH characteristics even at zero field; in such conditions, the material can only be in the “history-dependent” or “hard” states, never in the “soft” one.

Figure 5: Other magnetic characteristics of DFO.
Figure 5

(a) Proposed magnetic field vs. temperature phase diagram, involving the “hard”, “history-dependent” and “soft” WFM states as well as transition lines (red for the “history-dependent”/“hard” border, blue for the spin flip (SF) between two “hard” WFM states having opposite magnetization and green for the parallel to antiparallel (PA) transition). The square symbols gather data point obtained from Fig. 4; (b–j) FCC c-axis magnetization-versus-temperature under various applied fields for magnetized DFO. FCH measurements are also reported in panels (d–j). The results of panels (b–j) allow to complete and confirm the proposed, original phase diagram of panel a.

Moreover, for temperatures above 150 K, Fig. 4(c–f) further show that the magnetization within our standard hysteresis loops abruptly switches from positive to negative values, with the magnitude of this magnetization being conserved, when under a magnetic field. For instance, such a switching occurs for a magnetic field of −225 Oe at 300 K. These jumps are reported by means of blue squares in the magnetic field versus temperature phase diagram depicted in Fig. 5(a), and correspond to a transition between two “hard” WFM states having opposite long-range-ordered FFe–since FDy is rather small above 150 K as shown in Fig. 4(h).

It is also interesting to realize that, for T = 100 K, the standard hysteresis loop switches from a positive value of the magnetization equal to 0.13 μB/f.u (which corresponds to the FFe + FDy sum one can extract from Fig. 4(h) at T = 100 K, and as characterizing a “hard” WFM state) to a negative one equal to −0.03 μB/f.u (as representative of a “soft” WFM state, since the magnetization then linearly varies with H), for an applied magnetic field of about −10 Oe. Interestingly, this negative magnetization of −0.03 μB/f.u is neither equal to the value of -(FFe + FDy) = −0.128 μB/f.u nor to the value of -(FFe − FDy) = −0.113 μB/f.u one can deduce from Fig. 4(h). Similarly, the jump between the “hard” and “soft” states for magnetic field close to 140 Oe at T = 52 K does not correspond to a change of magnetization from (FFe + FDy) = 0.147 μB/f.u to (FFe − FDy) = 0.117 μB/f.u one can obtain from Fig. 4(h). To explain such results, it is reasonable to assume that “soft” and even “hard” WFM states, at and below 100K, are formed by domains having opposite directions for the antiferromagnetic (AFM) vector of the Fe sublattice. When no field is applied and the total magnetization is vanishing (e.g., at the beginning of the initial hysteresis loop for T = 100 K and 52 K, but also during the standard hysteresis loop at T = 52 K, see Fig. 4(a,b)), these AFM domains should also possess opposite directions for the magnetization of the Fe ions (positive or negative along the c-axis), since, within the Fe sublattice, the direction of the G-type antiferromagnetic vector dictates the direction of the WFM via a Dzyaloshinskii-Moriya (DM) interaction11. Moreover, these antiferromagnetic domains should also naturally favor opposite directions for the magnetization of the Dy ions (negative or negative along the c-axis), since FDy and FFe likely energetically prefer to be antiparallel to each other via another DM interaction19. However, at T = 100 K and H = −10 Oe during the standard hysteresis loop, the resulting “history-dependent” WFM state has a negative, small, but non-zero total magnetization, which can be explained by the facts that (i) there is a competition between the magnetic field desiring to make all the weak magnetizations of the Fe and Dy ions (i.e., belonging to the different AFM domains) aligned along its direction, and the aforementioned DM interactions11,19 that prefer to induce the WFM of the Fe ions and/or the WFM of the Dy ions to be aligned opposite to the applied magnetic field in some AFM domains; and (ii) the magnetic field wins more and more this competition as its strength grows. Note that items (i) and (ii) can also imply that the “hard” WFM state is formed by AFM domains below 100 K too, but with the WFMs of the Fe and Dy ions now completely following the magnetic field (i.e., not anymore reacting to the DM interactions11,19) and therefore saturating in value.

The analysis of the results of Fig. 4 therefore supports the idea that “soft” and even “hard” WFM states existing below 100 K can possess AFM domains, for which the ratio between domains with up magnetization and domains with down magnetization can be controlled by the magnitude and sign of the applied magnetic field. Note that, on the other hand, the “hard” WFM states above 150 K may be single monodomain states, which would explain the fact that the standard hysteresis loop has a perfect square shape and, therefore, that “soft” WFM states do not appear anymore in this standard loop.

Note that the facts that it is possible to access the antiferromagnetic-monodomain at relatively high temperatures, while it becomes essentially impossible (for the applied magnetic fields) at temperatures of 100 K and below, are actually the behaviors to expect. As a matter of fact, achieving the transformation to a monodomain state should be easier (i.e., it should require smaller applied fields) when the antiferromagnetic order is not strongly developed and/or the material has enough thermal energy, i.e., at higher temperatures.

Moreover and in order to complete the phase diagram of Fig. 5a, we decided to perform additional experiments, that consist in measuring the c-axis magnetization-versus-temperature curves of a DFO sample that is first magnetized at 300 K by a positive field along the c-axis of 200 Oe (respectively, negative field of −200 Oe) and then cooled down to 4 K and then heated up to 300 K under negative fields of −50, −75 or −100 Oe (respectively, positive fields of +50, +75 and + 100 Oe). The resulting FCC and FCH MT functions are displayed in Fig. 5(b, c, e–j). For the sake of completeness and for comparison, we also conducted similar measurements but for which no magnetic field is applied during cooling and heating after the DFO sample has been magnetized under a field of 200 Oe (see results in Fig. 5(d)). Note that this initial application of a field of 200 Oe generates a total magnetization of 0.07B/f.u. at 300 K (that is similar to the saturated value shown in Fig. 4f), and therefore results in the formation of a “hard” WFM state.

One can see that for fields equal to or above 75 Oe in magnitude, the total FCC magnetization can suddenly switch and nearly completely reverts its value, via a first jump, for a specific field-dependent temperature that is always larger than 130 K. Such data allow us to extend the blue lines of Fig. 5(a), and correspond to the spin flip (SF) transition between two “hard” WFMs states having opposite and long-range-ordered FFe magnetization. Moreover, for these fields equal to or above 75 Oe in magnitude, a second type of jump of the FCC occurs at smaller temperature (e.g., equal to 72 K for H = 75 Oe), below which the FCC and FCH curves become identical. Unlike the first type of jump and as evidenced in Fig. 5(b,f), this second type of jump is also happening for fields of 50 Oe and even 0 Oe magnitude and corresponds to the aforementioned PA transition below which FDy naturally prefers to be antiparallel (rather than parallel) to FFe. This second type of jumps therefore allows us to add more point to the green curve of Fig. 5(a), which is associated with the transition from “hard” WFM to “soft”/“history-dependent” WFM. Interestingly, the continuity one can see in Fig. 5a between the data extracted from Fig. 4 and those obtained from Fig. 5(b–j) demonstrates that the phase diagram of Fig. 5(a) is universal, in the sense that it applies to MH measurements done at fixed temperature (as in Fig. 4) but also to MT experiments conducted at fixed magnetic field (as in Fig. 5).

Discussion

Weak ferromagnetism has been systematically investigated in a high-quality single crystal of DFO grown by an optical floating zone method. Magnetic measurements reveal that the Γ4 magnetic state naturally prefers to present FFe and FDy moments being antiparallel to each other. We further found that relatively small magnetic fields can transform the antiparallel coupling into a parallel one, with the resulting state being coined “hard” WFM and for which the magnetization is nearly independent from the applied field. A magnetic field-versus-temperature phase diagram is constructed, mapping the “hard” WFM and “soft” WFM states but also a third state denoted as “history-dependent” WFM which can either be “hard” or “soft” depending on the history of the procedure used. This phase diagram also precisely predicts the sudden jumps of different natures (e.g., between two “hard” WFM states of opposite magnetization or between “soft” and “hard” WFM states), which is of obvious importance for devices exploiting spin switching phenomena.

Methods

A single crystal DFO was grown by an optical-floating-zone method (Crystal System Inc., type FZ-T-10000-H-VI-P-SH). The compounds of feed and seed rods were prepared by the solid state reaction of the raw materials Dy2O3(99.9%), and Fe2O3(99.99%) with the proper cation stoichiometry, which was calculated by the target compound. During the growth process, the molten zone moved upwards at a rate of 3 mm/h, with the seed rod (lower shaft) and the feed rod (upper shaft) counter rotating at 30 rpm in flowing air. Employing an X-ray Laue photograph (Try-SE. Co, Ltd.), we determined the crystallographic orientations, and cut the crystal into a 2.4 × 2.6 × 1.4 mm3 sample. The orientations were further verified by means of θ-2θ linear scans, using a high-resolutionX-ray diffraction (Bruker D8 Discover with 4-bounce Ge(220) monochromator and Cu Kα1 radiation (λ = 1.5406 Å)). The X-ray diffraction rocking curve on the (200), (020) and (004) diffraction peaks were also taken using this equipment. Measurements of the magnetization as a function of temperature and magnetic field were carried out using a Physical Property Measurement System (PPMS-9, Quantum Design) and a superconducting quantum interference device (SQUID) magnetometer (MPMS XL-5, Quantum Design), respectively, with the direction of the applied magnetic field being parallel to the corresponding crystallography axis. Different procedures were employed to acquire the temperature dependence of the magnetization (MT). For instance, we cooled the sample under no field down to 4 K, and then applied a magnetic field while heating the system; MT measurements were obtained during this latter heating process, which we denote as zero-field-cooling heating (ZFCH). We also cooled the system down to 4 K but now under an applied magnetic field, and measured the resulting MT curve during that process, which is coined field-cooling cooling (FCC) measurements. Finally, at the end of the FCC process, we also heated the system under the same magnetic field and measured the magnetization as a function of temperature. These measurements are denoted here as field-cooling heating (FCH). Furthermore, the magnetization vs. magnetic field isotherm curves were measured at several representative temperatures by changing the field at these temperatures.

Note that before all of those measurements, both the sample and the MPMS chamber are pretreated: (1) the sample was demagnetized at 500 °C, which is higher than the TN1 to disorder the orientation of WFM components; (2) a Pd standard sample, which is commonly used in MPMS to perform a precise small field correction before the measurements, is employed to obtain a quasi-zero-field measurements chamber.

Additional Information

How to cite this article: Cao, S. et al. Tuning the Weak Ferromagnetic States in Dysprosium Orthoferrite. Sci. Rep. 6, 37529; doi: 10.1038/srep37529 (2016).

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Acknowledgements

This work is supported by the National Key Basic Research Program of China (Grant No. 2015CB921600), the National Natural Science Foundation of China (NSFC, Nos 51372149, 11274221, 11274222, 11574194, 51572278), Eastern Scholar Program and Shuguang Program (Grant No. 12SG34) from Shanghai Municipal Education Commission, QiMingXing Project (14QA1402000). L.B. thanks the support of ARO Grant o.W911NF-16-1-0227. We also thank support from FNR Luxembourg through Grants FNR/P12/4853155/Kreisel (J.I. and H.J.Z.), and INTER/MOBILITY/15/9890527 GREENOX (L.B. and J.I.), and from the China Scholarship Council (P.C.).

Author information

Author notes

    • Shixun Cao
    • , Lei Chen
    •  & Weiyao Zhao

    These authors contributed equally to this work.

Affiliations

  1. Department of Physics, and International Center of Quantum and Molecular Structures, Shanghai University, Shanghai 200444, China

    • Shixun Cao
    • , Lei Chen
    • , Weiyao Zhao
    • , Kai Xu
    • , Guohua Wang
    • , Yali Yang
    • , Baojuan Kang
    • , Alessandro Stroppa
    •  & Wei Ren
  2. Materials Genome Institute, and Shanghai Key Laboratory of High Temperature Superconductors, Shanghai University, Shanghai 200444, China

    • Shixun Cao
    • , Jincang Zhang
    •  & Wei Ren
  3. State Key Laboratory of High Performance Ceramics and Superfine Microstructure, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai 200050, China

    • Lei Chen
    • , Weiyao Zhao
    •  & Ren-Kui Zheng
  4. Materials Research and Technology Department, Luxembourg Institute of Science and Technology (LIST), 5 avenue des Hauts-Fourneaux, L-4362 Esch/Alzette, Luxembourg

    • Hongjian Zhao
    • , Peng Chen
    •  & Jorge Íñiguez
  5. CNR SPIN, Via Vetoio, I-67100 Laquila, Italy

    • Alessandro Stroppa
  6. Physics Department and Institute for Nanoscience and Engineering, University of Arkansas, Fayetteville, AR 72701, USA

    • L. Bellaiche

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Contributions

S.X.C., L.C. and W.Z. contributed equally to this work. S.X.C., L.C. and W.Z. designed and performed the experiments. K.X. and G.H.W. participated the crystal growth process. B.J.K. participated the magnetic measurements. Y.L.Y., H.J.Z. P.C. participated the data analysis. S.X.C., L.C., W.Z., A.S., R.-K.Z., J.C.Z., W.R., J.I. and L.B. discussed the theoretical model. L.C. and W.Z. co-wrote the paper. S.X.C., W.R., L.B. and J.I. further modified the manuscript.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Shixun Cao or Wei Ren.

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DOI

https://doi.org/10.1038/srep37529

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