Article | Open

Hybrid supercapacitors for reversible control of magnetism

  • Nature Communications 8, Article number: 15339 (2017)
  • doi:10.1038/ncomms15339
  • Download Citation
Published online:


Electric field tuning of magnetism is one of the most intensely pursued research topics of recent times aiming at the development of new-generation low-power spintronics and microelectronics. However, a reversible magnetoelectric effect with an on/off ratio suitable for easy and precise device operation is yet to be achieved. Here we propose a novel route to robustly tune magnetism via the charging/discharging processes of hybrid supercapacitors, which involve electrostatic (electric-double-layer capacitance) and electrochemical (pseudocapacitance) doping. We use both charging mechanisms—occurring at the La0.74Sr0.26MnO3/ionic liquid interface to control the balance between ferromagnetic and non-ferromagnetic phases of La1−xSrxMnO3 to an unprecedented extent. A magnetic modulation of up to ≈33% is reached above room temperature when applying an external potential of only about 2.0 V. Our case study intends to draw attention to new, reversible physico-chemical phenomena in the rather unexplored area of magnetoelectric supercapacitors.


In quest of more energetically effective data storage and processing, sensing and actuation, the idea of using an electric field to control magnetism has been investigated in various fascinating ways1,2,3,4,5. A common and direct approach to realize the magnetoelectric (ME) effect is via manipulation of the electronic structure of a magnetic material by voltage-induced charge doping6. Typically, two possible charging mechanisms may occur at solid/solid or solid/liquid interfaces. The first involves non-faradaic electrostatic doping, where the charge carriers are electrostatically separated at the interface between a magnetic material and a ferroelectric7,8,9,10, a dielectric11 or an electrolyte12,13, in analogy to a parallel plate capacitor. The second implies faradaic electrochemical doping, where redox reactions with exchange of charge carriers14,15,16,17 occur across the interface between a magnetic material and a different chemical species, resembling the behaviour of an electrochemical cell.

It has been experimentally shown that the strength of the ME effect at the interface is directly related to the electrical capacitance6,9. In this regard, supercapacitors (SCs), so far primarily utilized for energy storage and delivery, provide attractive tools to reversibly and robustly control magnetism. They can accumulate charge electrostatically (as in electric-double-layer capacitors18,19), electrochemically (as in metal-oxide pseudocapacitors20,21,22,23) or by a combination of both (as in hybrid SCs24,25). In particular, pseudocapacitors can reach values of capacitance23 as high as 103 μF cm−2, which allows for surface charge densities appreciably beyond ferroelectrics (for example, 150 μC cm−2 for (ref. 26) BiFeO3). Further, they feature an exceptional degree of reversibility on charge/discharge cycling27,28.

To date, intensive efforts have been aimed at improving the SCs performance in terms of energy storage capacity and delivery, but the idea of utilizing a pseudocapacitor or a hybrid SC, per se, to control magnetism has not been embraced yet. In view of the recent discovery29 of pseudocapacitive reactions in LaMnO3, the class of magnetic manganese-based perovskite oxides naturally qualifies as a system of interest for modulation of magnetic properties via both electrostatic and electrochemical stimuli. In particular, La1−xSrxMnO3 (LSMO), owing to its high Curie temperature, can certainly be considered as a technologically relevant prototype system. This strongly correlated oxide features a rich magnetoelectronic phase diagram30 encompassing a variety of magnetic states31 that are determined by the charge state of the manganese ions (Mn3+/4+).

In this work we demonstrate that strong and reversible control of magnetism can be realized in ME hybrid SCs. Here by means of in situ synchronized superconducting quantum interference device (SQUID) magnetometry and cyclic voltammetry (CV), we track the magnetic response of a LSMO single-crystal thin film while modulating its surface charge density using an ionic liquid. We prove that the charging/discharging processes at the solid/liquid interface are those of a hybrid SC where electrostatic doping (electric-double-layer capacitance, C≈10 μF cm−2) is gradually replaced by faradaic electrochemical reactions (pseudocapacitance, C up to ≈180 μF cm−2) on progressive increase of the external voltage. We make use of both charging mechanisms to tune the magnetic interactions in LSMO by manipulating the oxidation state of the Mn ions. We exploit surface charge densities as high as ≈270 μC cm−2 to comprehensively explore the surface magnetoelectronic phase diagram of LSMO.


Capacitive and pseudocapacitive charging regimes

The experiments were performed on atomically smooth La0.74Sr0.26MnO3 thin films (≈13 nm), epitaxially grown on (001)-oriented SrTiO3 substrates (see Methods section).

An electrochemical tuning cell (see schematic in Fig. 1a), composed of a LSMO film (working electrode), a high-surface-area carbon cloth (counter electrode) separated by an insulating porous glass fibre soaked in ionic liquid (diethylmethyl(2-methoxyethyl)ammonium bis(trifluoromethylsulfonyl)imid, DEME-TFSI), was inserted into a SQUID magnetometer and connected to a potentiostat. The set-up allowed for quantitative and quasi-continuous in situ measurements of the magnetization response concurrently to modulation of the interface charge density. During the CV measurements, while the external potential V(t) was being ramped, the current density J(t) flowing towards the LSMO electrode was monitored, and by integrating it, the surface charge Q(t) at the LSMO/ionic liquid interface was calculated. Simultaneously, the magnetic response M(t) was measured. An illustrative example of a typical tuning experiment performed at 323 K, revealing the high degree of reversibility achieved above room temperature, is provided in Fig. 1b. In the initial state (before t0), the magnetization is constant. Afterwards, during CV cycling (from t0 to tf), the magnetic signal follows the surface charge modulation in a highly reproducible zigzag-like fashion with low-noise fluctuations. After tf, the magnetization recovers its initial value.

Figure 1: Sketch of the device and in situ measurement principle.
Figure 1

(a) Schematic of the electrochemical tuning cell: a La0.74Sr0.26MnO3 (LSMO) single-crystal thin film (≈13 nm) grown on a SrTiO3 substrate and a high-surface-area carbon cloth serve as working (WE) and counter (CE) electrodes, respectively. The electrodes are separated by an insulating glass fibre (not shown). On application of an external voltage, the ions of the ionic liquid (DEME+-TFSI) form physical or chemical bonds with the LSMO surface leading to electrostatic (electric-double-layer (EDL) capacitance) or electrochemical (pseudocapacitance (PS)) charge carrier doping, respectively. Both mechanisms allow for manipulating the magnetic state of LSMO. (b) Example of in situ tuning experiment performed at 323 K: the magnetic response (in red) reversibly follows the surface charge modulation (in blue), calculated by integrating the measured current density (in green), on repetitive cycling of the external potential (in black).

The figure of merit in CV experiments is the capacitance, defined as CQVQmax, where ΔQ is the difference between positive and negative maximum surface charge and ΔVQmax is the difference in the respective voltages. High values of capacitance are certainly desirable for tuning the magnetization because they directly result in large modulations of interface charge density ΔQ. Thus, the higher the charge carrier accumulation at the LSMO electrode is, the larger the number of Mn ions to undergo a change in oxidation state will be. This, in turn, enables a wider portion of the LSMO magnetoelectronic phase diagram to be probed in a full voltage sweep (see below for in-depth discussion).

Owing to a number of very sensitive control parameters, such as temperature, applied voltage and electrode/electrolyte chemical compatibility, a clear determination of whether the capacitance originates from electrostatic, electrochemical charging or a combination of both, is a non-trivial task32,33,34. Here, to reliably discern between faradaic and non-faradaic charging regimes, a series of systematic CV measurements was conducted for different temperatures, potential windows and voltage sweep rates.

Initially, a temperature-dependence survey was carried out from 330 down to 220 K, that is, slightly above the LSMO Curie point down to the DEME-TFSI glass transition35. The surface charge modulation was intentionally kept at the small value of ΔQ≈4 μC cm−2 using a working potential window of ΔV=VmaxVmin≈400 mV. Thus, electrochemical reactions at the LSMO/ionic liquid interface were hindered. Throughout the whole investigated temperature range, the J(V) characteristics (see Supplementary Fig. 2) featured the behaviour of an ideal capacitor with symmetric and rectangular shape of the charging/discharging processes and a remarkable reversibility on cycling. The calculated capacitance C≈10 μF cm−2 was virtually constant (see Supplementary Table 1) and consistent with the expected double-layer capacitance values reported for metallic conductive electrodes in ionic liquids36,37,38,39. These findings give a strong indication that under application of small external voltages, the CV measurements were performed within a regime dominated by electrostatic doping.

Afterwards, an isothermal charge-dependence study (Fig. 2a), with progressive expansion of the potential window ΔV from 0.2 up to 3.7 V, was carried out at the lowest temperature of 220 K. Interestingly, up to 2.4 V, the J(V) characteristics still exhibited a high level of reversibility with a nearly perfect rectangular shape. However, a systematic increase in current density, and therefore capacitance, was observed. These features represent the fingerprint of ideal pseudocapacitance21,22,40, denoting that electrode charging/discharging is driven also by interfacial electrochemical reactions. At a certain limit, when ΔV was considerably expanded up to 3.7 V, the J(V) curves displayed more pronounced electrochemical features.

Figure 2: Transition from capacitive to pseudocapacitive charging at 220 K.
Figure 2

(a) Current density—voltage characteristics upon expansion of the potential window (0.2 V<ΔV<3.7 V) using a scan rate of 3 mV s−1. Each curve corresponds to four consecutive CV cycles. The dashed lines qualitatively delimit the operative region expected for an ideal EDL capacitor. The increment in current density on increasing the applied ΔV indicates a progressive PS behaviour. The arrows indicate the points where irreversible redox reactions start to appear. (b) Calculated capacitance versus applied voltage for a scan rate of 3 mV s−1. The trend of C indicates a gradual transition from EDL capacitance to PS up to  V. Beyond this value, the steep increase in C denotes the predominance of PS. (c) Voltage ramp rate dependence of the current density for a particular potential window of 0.4 and 2.9 V. In b,c, the experimental errors are within a 5% accuracy.

The trend of the calculated capacitance, which increases from ≈10 up to ≈85 μF cm−2, is illustrated in Fig. 2b. The onset of pseudocapacitance seems to already develop at low voltages since the double-layer capacitance of standard metallic electrodes exhibits exactly the opposite behaviour39. Beyond a threshold value of  V, the steeper increase in C heralds a transition to a pseudocapacitive-dominated regime. Notably, at the biggest applied potential window of 3.7 V, the surface charge modulation reached a value of ≈270 μC cm−2.

It is known21,22,29 that pseudocapacitance involves redox reactions with faradaic charge transfer occurring at the surface and/or in the bulk of the electrode. Here ionic intercalation into LSMO is unlikely as the DEME41 and TFSI37 ions are nearly twice the size of the LSMO unit cell30. A minor contribution due to oxygen ions migration into LSMO may be attributed to the decomposition of residual traces of water42 present in the ionic liquid (see Methods section). This is compatible with the appearance of small irreversible redox peaks on expansion of the potential window up to 3.7 V (see arrows in Fig. 2a). The interpretation that surface pseudocapacitance plays a major role in the electrochemical doping of LSMO is corroborated by a voltage ramp rate study performed at the fixed potential windows of 0.4 and 2.9 V (Fig. 2c). On the one hand, the linear behaviour of the current density indicates the presence of fast surface charging/discharging processes20,43, resembling the charge-transfer kinetics of a capacitor rather than of an electrochemical cell. On the other hand, the calculated slopes confirm the radical increase in capacitance on expansion of the potential window.

These findings imply that the LSMO/ionic liquid system behaves as an archetypal hybrid SC. A plausible scenario is that the electric field-driven attraction of DEME and TFSI ions to the LSMO surface changes from physisorption to chemisorption when the potential window is increased. Consequently, the charging processes move from electrostatic (electric-double-layer capacitance) to electrochemical (surface redox pseudocapacitance) doping.

The behaviour of C on isothermal increase of the applied voltage was also studied at higher temperatures (see Supplementary Note 4 and Supplementary Fig. 5), where the thermally activated nature of electrochemical reactions16 precipitated the occurrence of pseudocapacitance. A maximum value of C≈180 μF cm−2 was achieved at around 320 K under the application of 1.8 V, leading to a surface charge density of ΔQ≈200 μC cm−2.

Electric field control of magnetism

In the following, the extensive and flexible control of the LSMO magnetic properties by means of both electrostatic and pseudocapacitive charging will be described.

A magnetic field-cooled measurement performed before in situ tuning experiments (Fig. 3a) revealed a Curie temperature of TC≈323 K. Afterwards, the effect of a nearly constant surface charge modulation ΔQ≈4 μC cm−2 on the LSMO magnetic response was investigated from above TC down to 220 K. The peak-to-peak variation in magnetization was defined as , that is, the difference between the maximum magnetization in hole accumulation and depletion states.

Figure 3: Temperature-dependence study on constant surface charge modulation ΔQ≈4 μC cm−2.
Figure 3

(a) Magnetic field-cooled curve performed before in situ tuning revealing a TC≈323 K. (b,c) Response of the magnetic modulation normalized per LSMO surface unit cell (b) and with respect to the volume magnetization (c). A crossover temperature Tcross≈258 K separates in-phase (white area) and anti-phase (grey area) magnetic responses with respect to the surface charge modulation. (df) Time-resolved magnetic response at TC (d), Tcross (e) and 220 K (f). Each time step in df on the abscissa corresponds to 500 s.

Figure 3b represents the behaviour of ΔMσ, determined by normalizing ΔM with respect to the LSMO surface unit cell area (u.c.2). The definition accounts for the interfacial nature of the tuning effect by assuming in first approximation a Thomas-Fermi screening length7,9 for the electric field of 0.2–0.4 nm. The trend of ΔM/M that gives the overall tuning effect compared to the untuned LSMO magnetization is depicted in Fig. 3c.

The study of the temperature dependence revealed that above TC the magnetic response M(t) was negligible while sweeping the surface charge Q(t). On reaching TC, a steep tuning effect with M(t) changing in-phase with Q(t) (Fig. 3d) was observed. After reaching a maximum magnetic modulation of ≈4.5%, a further decrease in temperature brought about a gradual reduction of the magnetic signal until it virtually vanished at Tcross≈258 K (Fig. 3e). Below this threshold, a crossover with a reverse in sign of the magnetic modulation was observed, that is, M(t) changed to anti-phase with respect to Q(t) (Fig. 3f). The existence of a crossover point has already been shown in other LSMO-tuning studies7,9,12,44, but here Tcross reaches the highest temperature reported.

A broader inspection of the surface magnetoelectronic phase diagram of LSMO started with tracking down the magnetic response during isothermal progressive expansion of the potential window (0.2 V<ΔV<3.7 V). It turned out that the high value of Tcross together with the achievable surface charge modulation of up to ΔQ≈270 μC cm−2 had a deep influence on the magnetism.

Focusing on the results obtained at 220 K, from small applied voltages up to 2.9 V, the magnetic signal was in anti-phase with respect to the surface charge modulation (plots a,b in Fig. 4a), in agreement with the results of temperature dependence. One of the main findings is that above this threshold voltage, the M(t) curve manifested a splitting on the electron accumulation side (plot c in Fig. 4a) with the distinctive in-phase characteristic observed above Tcross for a small potential window. As the potential window was further increased (plots d,e in Fig. 4a), this trend became more and more pronounced. This phenomenon allows for controlling the sign of the tuning effect under the application of a bias voltage. Indeed, by setting a negative bias Vb≈−1.3 V, the magnetic signal became immediately in-phase with the charge modulation (plot f in Fig. 4a). The versatility of LSMO magnetic responses achieved by simply adjusting the external voltage demonstrates an unprecedented control of the interfacial ME coupling.

Figure 4: Isothermal charge-dependence study at 220 K.
Figure 4

(a) Time-resolved magnetic responses on sequential increase of the surface charge modulation ΔQ from ≈1.5 up to ≈270 μC cm−2. The expected anti-phase response (plots a,b) reveals an in-phase splitting of the M(t) curve (plots c, d and e) on progressive electron doping, like the behaviour observed above Tcross for a small potential window. The application of a bias voltage Vb≈−1.3 V yielded an in-phase response (plot f). Each time step on the abscissa corresponds to 800 s. (b) Behaviour of the magnetization as a function of the surface charge doping. The slope of the M(Q) curves corresponds to the ME coupling coefficients α. The small variation in ΔM/M underlines the interfacial nature of the magnetic tuning effect at low temperature. In a,b, the white and grey areas qualitatively separate the data with the LSMO magnetization responding to the applied surface charge as above or below Tcross, respectively.

To quantify the strength of the ME effect we define the coupling coefficient αMQ. Its introduction as a figure of merit directly stems from the access to reliable, quantitative data on surface charge density and magnetization as given by the potentiostat and the SQUID magnetometer. The calculation of the slope of the M(Q) curves allowed for precise determination of α for both temperature-dependence and isothermal charge-dependence surveys. Regarding the former, as a direct consequence of the trend of the ΔM(T) curves, the sign of α was positive or negative above or below Tcross, respectively, with values ranging between +6.4 μB/h+ and −3.2 μB/h+ (see also Supplementary Note 2 and Supplementary Fig. 3). The latter study (Fig. 4b) revealed that on increasing ΔQ at a fixed temperature, the system behaved as being toggled back and forth across Tcross. Indeed, at 220 K it was possible to reversibly set the ME coupling coefficient to positive or negative values with respect to a plateau region where a maximum magnetization was reached (see also Supplementary Table 2). Furthermore, it is worth underlying that the magnetic tuning presented ΔM/M ratios of only a few per cent in all the measurements performed well below TC, corroborating the idea that surface effects are predominantly involved, as already concluded. Bigger magnitudes in magnetic modulation were encountered only in proximity of TC (see later discussion).

A tentative approach7,9,44 to interpret the interfacial ME phenomena starts with the LSMO bulk phase diagram30. Considering the doping region around x≈0.26, each introduced hole (electron), regardless of whether through electrochemical or electrostatic doping, results in a shift of TC towards higher (lower) temperatures. Concurrently (and with the opposite trend), the ground state magnetization (MMn=(4−x)μB u.c.−1) decreases (increases) on hole (electron) doping in accordance with a band filling model where each introduced positive (negative) carrier contributes with a magnetic moment of −(+)1 μB. The competition between these two effects, with the former prevailing in proximity of TC and the latter at low temperatures, is clearly evidenced in the temperature-dependence survey by the presence of a crossover point Tcross, which separates the in-phase and anti-phase regimes of M(t) over Q(t). Further details are discussed in Supplementary Note 3 and Supplementary Fig. 4.

Although this phenomenological picture is sufficient to qualitatively describe the observed general trends, it notably fails7,9,44 when quantitative data are taken into account. To capture the essence of a plausible microscopic picture, one should bear in mind the following considerations based on the experimental findings at 220 K (see also Supplementary Table 2), which are unaffected by the possible critical effects occurring close to TC.

First, the interfacial nature of the magnetic tuning effect together with charge density modulations of up to ΔQ≈270 μC cm−2 (corresponding to about ±1h+ u.c.−2) imply that the LSMO surface magnetoelectronic configuration can be virtually probed across the entire range of possible hole-doped states of the phase diagram. It is known31 that the interaction between adjacent Mn3+/4+, Mn3+/3+ and Mn4+/4+ ions promotes ferromagnetic (FM), A-type and G-type antiferromagnetic (AF) ground states, respectively. Furthermore, at non-zero temperatures, paramagnetic (PM) states come into play as well.

Second, the absolute value of the ME coupling coefficient is . This is not in line with the 1 μB/h+ predicted by a band filling model, but rather points to the annihilation (creation) of an entire magnetic moment carried by one Mn ion (MMn≈3.7 μB u.c.−1). Additionally, is nearly constant over a broad range of investigated ΔQ, already when pseudocapacitance contributes to surface charging. This suggests that electrostatic and electrochemical doping, in spite of the different physical and chemical origin, have a similar functional role in the magnetic phase control.

These experimental facts indicate that a microscopic model still coherent with the major phenomenological features is conceivable only by incorporating a magnetoelectronic phase separation phenomenon45,46,47 at the LSMO surface. In a simplified scenario (see Fig. 5), the local electric field at the electrode/ionic liquid interface induces the accumulation of charge carriers at the LSMO terminating layers. The consequent change in oxidation state of the Mn ions promotes either the expansion or shrinkage of FM and non-FM (PM or AF) domains, at the expense of each other. Considering plot e in Fig. 4b, the initial increase in magnetization on electron doping can be explained as a gradual optimization of the Mn3+/4+ ratio, hence fostering the growth of FM-coupled domains (Fig. 5b). During sweeping to higher electron concentrations, the oxidation state of the surface manganese ions progressively shifts towards a Mn3+/3+ balance. Either AF or PM ordering is favoured (Fig. 5c), thus decreasing the overall magnetization. By reversing the voltage sign, the magnetization recovers up to a maximum point due to the restored Mn3+/4+ interactions. By sweeping further along the hole accumulation side, the amount of Mn4+/4+ domains increases (Fig. 5d). Owing to the expansion of non-FM states, a decrease in the total magnetization is again observed.

Figure 5: Mechanism of electric field tuning of magnetoelectronic phase separation at the LSMO/ionic liquid interface.
Figure 5

For the sake of clarity, not the entire perovskite unit cell of LSMO, but only the oxygen octahedron containing one Mn ion is shown. The sketches should be read together with the trend of the M(Q) curves in Fig. 4b. (a) Initial surface magnetoelectronic configuration of LSMO with two distinguished FM and non-FM domains. (b) Expansion of the FM domain on electron doping (optimization of Mn3+/4+ balance). (c) Shrinkage of the FM domain on further electron doping (increase in Mn3+/3+ balance). (d) Shrinkage of the FM domain on hole doping (increase in Mn4+/4+ balance).

A series of analogous isothermal charge-dependence studies were also carried out at temperatures above Tcross. The results of the experiments performed at 270 K confirm the findings acquired at 220 K and corroborate the proposed microscopic model of electric field tuned magnetoelectronic phase separation (see Supplementary Note 4 and Supplementary Fig. 5).

The sensitivity of the system to surface charge modulation was also probed at the immediate proximity of TC. A remarkable overall magnetic modulation ΔM/M≈33% was reached using a potential window of only ΔV≈1.8 V (Fig. 6a). The high-tuning effect can be explained by a deeper penetration depth of the electric field close to the insulator-metal transition, which corresponds48 also to the para-ferromagnetic transition. Although the Thomas-Fermi screening length7,9 in purely metallic manganites reported in the literature is typically of 0.2–0.4 nm, it has been demonstrated that around TC the electric field can effectively extend up to 5 nm in electrolyte-gated La0.8Ca0.2MnO3 films33. Furthermore, in presence of magnetoelectronic phase separation a strongly inhomogeneous and much deeper penetration of the electric field is expected47.

Figure 6: Tuning of magnetism in proximity of TC and LSMO surface characterization.
Figure 6

(a) Time-resolved magnetic response featuring a ≈33% tuning effect on modulation of the surface charge density (ΔQ≈200 μC cm−2). The expected in-phase response (white area) of M(t) with respect to Q(t) reveals an anti-phase splitting (grey area) on the hole doping branch, akin to the behaviour encountered below Tcross for a small potential window. (b,c) Atomic force micrographs of the LSMO surface before (b) and after (c) in situ tuning. In both b,c, scale bar, total height scale root-mean-square roughness are about 1 microm, 1.5 nm and 0.2 nm, respectively.

Eventually, after performing more than 1,000 CV cycles under different temperatures and applied voltages, atomic force microscopy was employed to analyse the surface morphology of LSMO. The striking similarity of the atomic force micrographs before and after in situ tuning (Fig. 6b,c), featuring in both cases an atomically smooth surface with one or half unit cell steps, demonstrates the astonishing non-destructive nature of electric-double-layer and pseudocapacitive charging.


Our results demonstrate that fully reversible and robust ME coupling can be realized in LSMO/ionic liquid hybrid SCs by exploiting surface electrostatic and electrochemical doping. From a fundamental scientific perspective, the interdisciplinary character of our study aims at bridging the fields of MEs and SCs. The quantitative data, such as precisely determined values of α, extracted from the temperature and charge-dependence surveys provide a solid base for further theoretical modelling of the interfacial tuning phenomena. On the more practical side, the devices tested in a broad temperature range and at low voltages show an unprecedented reversibility and flexibility in controlling both the magnitude and sign of the magnetic response using electric-double-layer and surface pseudocapacitive charging. In general, we propose that surface pseudocapacitance should expand the portfolio of tools to control magnetism, which already comprises strain, electrostatic doping and bulk-intercalation chemistry. Our work, although focusing on LSMO manganites, intends to pave the way for a broader, in-depth research on other potential magnetically functional SCs, such as cobaltites, ferrites and nickelites. The huge and reversible charge densities attainable at low voltages via surface pseudocapacitance may lead to giant magnetic tuning effects with possible applications in future, low-power electric field and spintronic-based microelectronics.


Synthesis and characterization of LSMO films

La0.74Sr0.26MnO3 thin films were grown via large-distance rf-magnetron sputtering at a pressure of 0.018 mbar and a deposition temperature of ≈650 °C on single-crystal SrTiO3 substrates49. Before in situ tuning, the films were comprehensively investigated with a variety of characterization techniques (see Supplementary Note 1 and Supplementary Fig. 1).

Electrochemical tuning cell preparation

An electrochemical cell composed of a LSMO film (surface area of ≈0.4 cm2) as the working electrode, a high-surface-area carbon fibre cloth (SBET≈2,400 m2 g−1, Whatman) as the counter electrode, a glass fibre filter disc (GF/A, Whatman) as the separator and an ionic liquid (DEME-TFSI 98.5%, Sigma-Aldrich) as the non-aqueous electrolyte, was assembled under glove box conditions (with [O2] <1 p.p.m. and [H2O] <1 p.p.m.). Before the cell preparation, the ionic liquid was purified from water contamination by keeping it under vacuum conditions (10−3 mbar) at 120 °C for 24 h; afterwards Karl Fischer titration revealed an H2O level <50 p.p.m. Gold and kapton-coated copper wires were connected internally to working and counter electrodes, respectively, and externally to electrical feedtroughs which allowed the transfer of signals with a potentiostat (μAutolab Type3). Once prepared, the tuning cell was quickly transferred into a SQUID magnetometer (Quantum Design MPMS XL-5). The voltage and current outputs of the potentiostat were put in communication with two multimeters (Keithley 2001), which delivered the signals to the SQUID magnetometer. Finally, a software script allowed for real-time control and detection of magnetization, voltage and current signals.

In situ ME tuning measurements

All the SQUID measurements were performed at an external magnetic field of 100 Oe applied parallel to the plane of the film; reversing the sign of the field resulted in a mirror image of the time-resolved magnetic modulation. Unless differently specified, all the CV measurements were carried out at a fixed voltage ramp rate of 3 mV s−1. Owing to the two-electrode configuration of the tuning cell, all the working potential windows were set with respect to open circuit potential (OCP≈−100 mV) as their starting point, and the voltage data were presented accordingly.

Data availability

All relevant data are available from the corresponding authors on reasonable request.

Additional information

How to cite this article: Molinari, A. et al. Hybrid supercapacitors for reversible control of magnetism. Nat. Commun. 8, 15339 doi: 10.1038/ncomms15339 (2017).

Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.


  1. 1.

    & The renaissance of magnetoelectric multiferroics. Science 309, 391–392 (2005).

  2. 2.

    et al. Reversible electric control of exchange bias in a multiferroic field-effect device. Nat. Mater. 9, 756–761 (2010).

  3. 3.

    , , , & Giant sharp and persistent converse magnetoelectric effects in multiferroic epitaxial heterostructures. Nat. Mater. 6, 348–351 (2007).

  4. 4.

    et al. Large voltage-induced magnetic anisotropy change in a few atomic layers of iron. Nat. Nanotechnol. 4, 158–161 (2009).

  5. 5.

    et al. Electric-field control of magnetic order above room temperature. Nat. Mater. 13, 345–351 (2014).

  6. 6.

    , & Control of magnetism by electric fields. Nat. Nanotechnol. 10, 209–220 (2015).

  7. 7.

    et al. Magnetoelectric effects in complex oxides with competing ground states. Adv. Mater. 21, 3470–3474 (2009).

  8. 8.

    et al. Origin of the magnetoelectric coupling effect in Pb(Zr0.2Ti0.8)O3/La0.8Sr0.2MnO3 multiferroic heterostructures. Phys. Rev. Lett. 104, 127202 (2010).

  9. 9.

    , , & In situ magnetometry studies of magnetoelectric LSMO/PZT heterostructures. Phys. Rev. B 87, 094416 (2013).

  10. 10.

    , & Electric modulation of magnetization at the BaTiO3/La0.67Sr0.33MnO3 interfaces. Appl. Phys. Lett. 100, 232904 (2012).

  11. 11.

    , , & Near-room-temperature control of magnetization in field effect devices based on La0.67Sr0.33MnO3 thin films. J. Appl. Phys. 108, 113906 (2010).

  12. 12.

    , , , & Room temperature reversible tuning of magnetism of electrolyte-gated La0.75Sr0.25MnO3 nanoparticles. J. Appl. Phys. 113, 033913 (2013).

  13. 13.

    , , , & Large magnetoresistance and electrostatic control of magnetism in ordered mesoporous La1−xCaxMnO3 thin films. Chem. Mater. 26, 5745–5751 (2014).

  14. 14.

    , & Voltage-controlled domain wall traps in ferromagnetic nanowires. Nat. Nanotechnol. 8, 411–416 (2013).

  15. 15.

    et al. Intercalation-driven reversible control of magnetism in bulk ferromagnets. Adv. Mater. 26, 4639–4644 (2014).

  16. 16.

    et al. Magneto-ionic control of interfacial magnetism. Nat. Mater. 14, 174–181 (2015).

  17. 17.

    et al. Toward on-and-off magnetism: reversible electrochemistry to control magnetic phase transitions in spinel ferrites. Adv. Funct. Mater. 26, 7507–7515 (2016).

  18. 18.

    & Carbon properties and their role in supercapacitors. J. Power Sources 157, 11–27 (2006).

  19. 19.

    et al. Carbon-based supercapacitors produced by activation of graphene. Science 332, 1537–1541 (2011).

  20. 20.

    , & Pseudocapacitive oxide materials for high-rate electrochemical energy storage. Energ. Environ. Sci. 7, 1597–1614 (2014).

  21. 21.

    Transition from ‘supercapacitor’ to ‘battery’ behavior in electrochemical energy storage. J. Electrochem. Soc. 138, 1539–1548 (1991).

  22. 22.

    , & The role and utilization of pseudocapacitance for energy storage by supercapacitors. J. Power Sources 66, 1–14 (1997).

  23. 23.

    , & Charge storage mechanism of MnO2 electrode used in aqueous electrochemical capacitor. Chem. Mater. 16, 3184–3190 (2004).

  24. 24.

    & Supercapacitors: A Brief Overview The MITRE Corporation, McLean (2006).

  25. 25.

    , & Hybrid supercapacitor based on coaxially coated manganese oxide on vertically aligned carbon nanofiber arrays. Chem. Mater. 22, 5022–5030 (2010).

  26. 26.

    & Effect of epitaxial strain on the spontaneous polarization of thin film ferroelectrics. Phys. Rev. Lett. 95, 257601 (2005).

  27. 27.

    , & Novel electrode materials for thin-film ultracapacitors: comparison of electrochemical properties of sol-gel-derived and electrodeposited manganese dioxide. J. Electrochem. Soc. 147, 444–450 (2000).

  28. 28.

    , & Microstructural effects on charge-storage properties in MnO2-based electrochemical supercapacitors. ACS Appl. Mater. Interfaces 1, 1130–1139 (2009).

  29. 29.

    , , , & Anion charge storage through oxygen intercalation in LaMnO3 perovskite pseudocapacitor electrodes. Nat. Mater 13, 726–732 (2014).

  30. 30.

    et al. Structural and magnetic phase diagrams of La1−xSrxMnO3 and Pr1−ySryMnO3. Phys. Rev. B 67, 094431 (2003).

  31. 31.

    , & Mixed-valence manganites. Adv. Phys. 58, 571–697 (2009).

  32. 32.

    et al. Suppression of metal-insulator transition in VO2 by electric field-induced oxygen vacancy formation. Science 339, 1402–1405 (2013).

  33. 33.

    , , , & Large electric field effect in electrolyte-gated manganites. Phys. Rev. Lett. 102, 136402 (2009).

  34. 34.

    , , & Electrostatic charge accumulation versus electrochemical doping in SrTiO3 electric double layer transistors. Appl. Phys. Lett. 96, 252107 (2010).

  35. 35.

    , & Electrochemical properties of novel ionic liquids for electric double layer capacitor applications. Electrochim. Acta 49, 3603–3611 (2004).

  36. 36.

    in Electrochemical Aspects of Ionic Liquids Vol. 1, Ch. 17 (John Wiley & Sons, Inc., 2005).

  37. 37.

    et al. Relation between the ion size and pore size for an electric double-layer capacitor. J. Am. Chem. Soc. 130, 2730–2731 (2008).

  38. 38.

    & Carbon-ionic liquid double-layer capacitors. J. Phys. Chem. Solids 65, 281–286 (2004).

  39. 39.

    , & Double layer in ionic liquids: overscreening versus crowding. Phys. Rev. Lett. 106, 046102 (2011).

  40. 40.

    et al. Pseudocapacitive mechanism of manganese oxide in 1-ethyl-3-methylimidazolium thiocyanate ionic liquid electrolyte studied using X-ray photoelectron spectroscopy. Langmuir 25, 11955–11960 (2009).

  41. 41.

    & Ionic liquids based on diethylmethyl(2-methoxyethyl)ammonium cations and bis(perfluoroalkanesulfonyl)amide anions: influence of anion structure on liquid properties. Phys. Chem. Chem. Phys. 13, 20302–20310 (2011).

  42. 42.

    et al. Metal-insulator transition induced by oxygen vacancies from electrochemical reaction in ionic liquid-gated manganite films. Adv. Mater. Interfaces 2, 1500407 (2015).

  43. 43.

    , , & Ordered mesoporous alpha-MoO3 with iso-oriented nanocrystalline walls for thin-film pseudocapacitors. Nat. Mater. 9, 146–151 (2010).

  44. 44.

    et al. Temperature dependence of the magnetoelectric effect in Pb(Zr0.2Ti0.8)O3/La0.8Sr0.2MnO3 multiferroic heterostructures. Appl. Phys. Lett. 97, 042506 (2010).

  45. 45.

    , & Phase separation scenario for manganese oxides and related materials. Science 283, 2034–2040 (1999).

  46. 46.

    et al. Intrinsic inhomogeneities in manganite thin films investigated with scanning tunneling spectroscopy. Phys. Rev. Lett. 89, 237203 (2002).

  47. 47.

    , , , & Electric field tuning of phase separation in manganite thin films. Phys. Rev. B 89, 014425 (2014).

  48. 48.

    et al. Insulator-metal transition and giant magnetoresistance in La1−xSrxMnO3. Phys. Rev. B 51, 14103 (1995).

  49. 49.

    et al. Large-distance rf- and dc-sputtering of epitaxial La1−xSrxMnO3 thin films. Thin Solid Films 520, 5521–5527 (2012).

Download references


We are grateful to R.A. Brand, J. Schmalian, B. Jeevanesan and M. Rosiejka for their interest and fruitful discussions. We thank A. Houari and A. Beck for the TEM and RBS characterization of the LSMO films, respectively. S.D. and H.H. thank the financial support from the DFG Grants DA 1781/1-1 and HA 1344/34-1, respectively. We acknowledge support by Deutsche Forschungsgemeinschaft and Open Access Publishing Fund of Karlsruhe Institute of Technology.

Author information

Author notes

    • Subho Dasgupta

    Present address: Department of Materials Engineering, Indian Institute of Science (IISc), Bangalore 560012, India


  1. Institute of Nanotechnology (INT), Karlsruhe Institute of Technology (KIT), Hermann-von-Helmholtz-Platz 1, 76344 Eggenstein-Leopoldshafen, Germany

    • Alan Molinari
    • , Philipp M. Leufke
    • , Christian Reitz
    • , Subho Dasgupta
    • , Ralf Witte
    • , Robert Kruk
    •  & Horst Hahn
  2. KIT-TUD-Joint Research Laboratory Nanomaterials, Technical University Darmstadt, Jovanka-Bontschits-Strasse 2, 64287 Darmstadt, Germany

    • Horst Hahn


  1. Search for Alan Molinari in:

  2. Search for Philipp M. Leufke in:

  3. Search for Christian Reitz in:

  4. Search for Subho Dasgupta in:

  5. Search for Ralf Witte in:

  6. Search for Robert Kruk in:

  7. Search for Horst Hahn in:


H.H. and R.K. supervised the study. A.M. prepared and characterized the samples with the support of P.M.L. and R.W., respectively. A.M. performed the in situ tuning experiments with the help of R.K., C.R. and S.D. A.M. analysed the data with the support of R.K., S.D. and P.M.L. A.M. wrote the manuscript with assistance from R.K. and input from H.H., C.R., R.W. and S.D. All authors discussed the results and commented on the manuscript.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Alan Molinari or Horst Hahn.

Supplementary information

PDF files

  1. 1.

    Supplementary Information

    Supplementary Figures, Supplementary Tables, Supplementary Notes and Supplementary References.

  2. 2.

    Peer Review File


By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.

Creative Commons BYThis work is licensed under a Creative Commons Attribution 4.0 International License. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in the credit line; if the material is not included under the Creative Commons license, users will need to obtain permission from the license holder to reproduce the material. To view a copy of this license, visit