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# Emergence of the Stoner-Wohlfarth astroid in thin films at dynamic regime

## Abstract

The Stoner-Wohlfarth (SW) model is the simplest model that describes adequately the magnetization reversal of nanoscale systems that are small enough to contain single magnetic domains. However for larger sizes where multi-domain effects are present, e.g., in thin films, this simple macrospin approximation fails and the experimental critical curve, referred as SW astroid, is far from its predictions. Here we show that this discrepancy could vanish also in extended system. We present a detailed angular-dependent study of magnetization reversal dynamics of a thin film with well-defined uniaxial magnetic anisotropy, performed over 9 decades of applied field sweep rate (dH/dt). The angular-dependent properties display a gradual transition from domain wall pinning and motion-like behaviour to a nucleative single-particle one, as dH/dt increases. Remarkably, in the high dynamic regime, where nucleation of reversed domains is the dominant mechanism of the magnetization reversal (nucleative regime), the magnetic properties including the astroid become closer to the ones predicted by SW model. The results also show why the SW model can successfully describe other extended systems that present nucleative regime, even in quasi-static conditions.

## Introduction

The study of magnetization reversal processes is an important issue in Nanomagnetism today1, both from fundamental and technological points of view. The use of magnetic materials in all applications ranging from compass needles to electrical motors, cellular phones and personal computers has triggered the search for materials with particular properties concerning both their static and dynamic reversal behavior. For instance, magnetization reversal features (i.e., relevant mechanism, reversal times, reversal fields) determine how the magnetization preserves its state in powerful permanent magnet applications, based on nanograin ferromagnetic structures consolidated in bulk systems2, as well as how the information can be read and written in spintronic devices3, based on multilayered thin film architectures. Current and future technologies require hence basic understanding and control of hysteresis and magnetization reversal processes4.

The physical mechanisms responsible for the hysteresis and magnetization reversal in magnetic nanostructures become more complex to interpret as the dimensionality increases5,6,7, from zero-dimensional (nanoparticles) to two-dimensional (thin films). In general, hysteresis include reversible (rotation) and irreversible (switching) magnetic transitions. Magnetization reversal can take place in different ways, depending on object size and physical parameters. The exchange interaction, magnetic anisotropy and magnetostatics are among the most important physical parameters involved8. First, exchange interaction favors uniform magnetization configurations. Second, magnetic anisotropy favors the orientation of the magnetization vector along certain preferred directions. And third, magnetostatic interaction favors configurations giving null average magnetic moment, in contrast with anisotropy and exchange. In addition to these intrinsic parameters, the hysteresis depends on extrinsic parameters such as temperature, applied field angle, and applied field sweep rate. Models for collective reversal provide good agreement between experiment and theory in the case of small particles9, both in uniform reversal modes (SW model5), as shown for nanoparticles10, or in non-uniform ones, as in nanowires11. The geometric representation of SW model is recognized by the polar plot representation (as a function of the applied field angle) of the reversal fields, referred to both the coercivity and the (irreversible) switching field, called SW-astroid12, which are represented with solid lines in the left and right panel of Fig. 1, respectively. What stands out the most is that the SW model predicts identical switching fields at the easy-axis (e.a.) and hard-axis (h.a.) magnetization directions, whereas the curling model predicts smaller values at e.a. direction13, depending on the aspect ratio of the one-dimensional magnetic nanostructure. For microscopic objects and extended thin films, reversible and irreversible magnetization transitions represent different reversal processes, and they are often a manifestation of the magnetic symmetry of the system14. Reversible transitions are related to rotation processes, whereas irreversible ones are related to nucleation of reversed magnetic domains (usually created at inhomogeneities or defects) and subsequent propagation of their magnetic domain walls, under the field pressure15.

The magnetic properties are hence determined by a combination of nucleation and domain wall propagation behaviors with their associated energy barriers. In addition, the relevance of these processes depends on the direction of the applied magnetic field with respect to certain characteristic axes of the magnetic system, i.e., magnetic anisotropy axes16, and depends as well on the field rate of change, since they are different in quasi-static and dynamic regimes17. In magnetic thin films with in-plane dimensions considerably larger than the domain wall width the irreversible processes usually starts at magnetic fields that are significantly lower than expected from SW model, the so-called Brown’s paradox18. In this case, the lateral dimensions strongly affect the magnetic behavior. For instance, experimental astroids with shapes approaching those predicted by SW model have been found in $$200\times 500$$ nm2 size thin film-based magnetic elements, but become much less ideal when the size increases, even though still in the submicron size19. In this sense, predictions based on the SW model are significantly far from experimental data for extended thin film-based magnetic nanostructures.

In this letter we show the emergence of a single-particle like magnetic behavior in extended thin films at dynamic regime. This can be easily visualized in Fig. 1 by observing that the dynamic coercive field ($${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$) and switching field ($${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$) are approaching to the SW prediction as the applied field sweep rate (dH/dt) increases. We have carried out a detailed dynamical study on the angular dependence of the magnetic properties on model extended thin films with well-defined uniaxial magnetic anisotropy. In particular, we have used Co FM thin films grown on Si substrates with Ta buffer layer. Samples were exposed to 0.2 Tesla in-plane external magnetic field during growth, in order to induce a well-defined uniaxial magnetic anisotropy ($${K}_{{\rm{U}}}$$) in the FM layer, parallel to the field direction. Experimental details are given in Methods and in the Supplementary information. The magnetization reversal dynamics of the two in-plane magnetization components, i.e., parallel ($${M}_{||}$$) and transverse ($${M}_{\perp }$$) to the external applied field, have been investigated over 9 decades of dH/dt and in the whole angular range. Thermal activated dynamical effects are found during irreversible processes and depend strongly on the orientation of the anisotropy axis with respect to the external field (referred as the angle $${\alpha }_{{\rm{H}}}$$). The effects are more relevant near the e.a. direction ($${\alpha }_{{\rm{H}}}{\mathrm{=0}}^{\circ }$$) and vanishes near the h.a. direction ($${\alpha }_{{\rm{H}}}{\mathrm{=90}}^{\circ }$$). In contrast, the reversible transitions are not affected by dynamical effects. The data have been interpreted in the framework of the magnetic domain pinning and rotation models for quasi-static and dynamic conditions, respectively.

The reversal processes can be determined directly by a simple inspection of the in-plane vectorial magnetization loops20,21, highlighting the importance of vectorial-resolved magnetometry. Full angular-dependent studies were carried out at selected dH/dt values. A detailed analysis in quasi-static condition is given in the Supplementary information. Figure 2 shows representative parallel ($${M}_{||}$$) and transversal ($${M}_{\perp }$$) magnetization loops at selected $${\alpha }_{{\rm{H}}}$$ acquired at different dH/dt. For a given $$dH/dt$$, in general, irreversible (sharp) transitions and/or fully reversible (smoother) transitions are observed in both $${M}_{||}(H)$$ and $${M}_{\perp }(H)$$ loops, which correspond to nucleation of magnetic domains followed by domain wall propagation and to rotation processes, respectively. The relative weight of these two reversal mechanisms depends on $${\alpha }_{{\rm{H}}}$$ and $$dH/dt$$ and reveals the uniaxial magnetic anisotropy of the film.

For a given $${\alpha }_{{\rm{H}}}$$, the shapes that both $${M}_{||}(H)$$ and $${M}_{\perp }(H)$$ loops have before the irreversible transition are similar for the whole dynamic range of dH/dt investigated, as can be seen on the left and right graphs of Fig. 2, respectively: dynamical effects result in a lengthening of the reversible processes, but without changing their shape, which indicates that reversible processes are non-thermally activated. Dynamical effects are only observed in the irreversible transitions: increment of the reversal fields and broadening of the transitions as the applied field sweep rate is increased. As for the first aspect, the reversal field enhancement indicates that the irreversible processes are thermally activated. For the second aspect, the broadening of the irreversible transitions suggests that the reversal is governed by two different mechanisms depending on the dynamic regime: at lower dH/dt the reversal is mainly governed by domain wall propagation processes (characterized by more abrupt jumps), while at higher sweep rates, domain nucleation processes dominate (softening the irreversible jumps), as discussed in more detail below.

Over the last decades, several studies have addressed the magnetization reversal dynamics in several magnetic thin film-based nanostructures at different timescales. In general, precessional reversal of magnetization takes place at subnanosecond timescales (ultra-fast dynamic regime)22, while nucleative and propagative processes can take variable amounts of time7, from submicrosecond (high dynamic regime) to large fractions of a second (quasi-static or low dynamic regime)23. For instance, hysteresis loop measurements as a function of the applied magnetic field sweep rate (dH/dt) support the picture of nucleation-dominated reversal in the high dynamic regime and wall propagation-dominated reversal in the low dynamic regime24,25. This scenario has been found in dynamical studies of single ferromagnetic (FM) layers with both in-plane26,27 and out-of-plane28 anisotropy as well as in more complex structures, such as in-plane29,30 and out-of-plane31 exchange-biased FM/antiferromagnetic systems and trilayer FM1/non magnetic/FM2 magnetic structures32. The crossover between propagative and nucleative regimes depends on the strength of the anisotropy of the system: higher anisotropy favors earlier nucleative regimes. It is worth mentioning that all these studies were performed only at the e.a. direction, and with sensitivity only to the magnetization component parallel to the external field.

In our study, in addition, we can determine the angular dependence of the dynamical effects. For instance, by comparing the loops of Fig. 2 acquired at the minimum and maximum dH/dt values for the different angles, we find out that the rise of the dynamic effects are more pronounced at the e.a. direction (top graph), i.e., $${\alpha }_{{\rm{H}}}{=0}^{\circ }$$, diminishing progressively as the applied field angle increases (middle graphs), and vanishing at the h.a. direction (bottom graph), i.e., $${\alpha }_{{\rm{H}}}{=90}^{\circ }$$. Notice that as dH/dt increases, the experimental loops approaches the ones predicted with the SW model (solid lines in Fig. 2). In turn, the remanent magnetization (or remanence) $${M}_{{\rm{R}}}$$, i.e., magnetization at zero field, of both magnetization components is independent of the applied field sweep rate in the whole angular range. Figure 3 shows similar angular dependence at two different dH/dt values that differ in six orders of magnitude, i.e., for quasi-static and high dynamic conditions. The corresponding polar plots depicted in Fig. 2(b) show the characteristic (two-fold) symmetry of a well-defined uniaxial magnetic anisotropy system: $${M}_{{\rm{R}},\parallel }({\alpha }_{{\rm{H}}})$$ and $$|{M}_{\perp ,{\rm{R}}}({\alpha }_{{\rm{H}}})|$$ display “two-lobes” shape rotated 90° with respect to each other. This unambiguously indicates that the orientation of the magnetization vector at remanence does not present dynamical effects. In fact, this is preserved until the irreversible transition takes place. These features are in accordance with the relevance of the (non-thermal activated) reversible and (thermal activated) irreversible transitions. Therefore, the magnetic symmetry is preserved and larger dynamic effects are found where irreversible processes are more relevant during reversal.

Thermal vs. non-thermal activation effects on magnetization reversal dynamics manifest directly through the analysis of the dynamic transition reversal fields of both magnetization components, referred as coercive field $${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$ and switching field $${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$, and defined as the fields at which $${M}_{||}({\mu }_{{\rm{0}}}{H}_{{\rm{C}}}\mathrm{)=0}$$ and $${M}_{\perp }({\mu }_{{\rm{0}}}{H}_{{\rm{S}}}\mathrm{)=0}$$, respectively. Figure 4 shows the corresponding dynamic evolution of coercive and switching fields at representative $${\alpha }_{{\rm{H}}}$$. The global behavior is summarized as an increase in $${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$ as dH/dt increases, but clearly two dynamical behaviors at low and high sweep rates can be distinguished, where $${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$ varies very slowly at low sweep rate, and increases more rapidly at high rates. The crossover between the two regimes, marked with vertical arrows in Fig. 4, takes place at higher dH/dt for larger angles (yellow arrow shifts to the right as angle is increased). In contrast, $${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$ shows three dynamical evolutions for different angular ranges. In general, all can be associated to the relevant mechanism during reversal, where (thermally activated) irreversible and (non-thermally activated) reversible processes govern the dynamics around the e.a. and h.a. directions, respectively. For intermediate angles, the dynamic fields result from the competition between them.

Around the e.a. direction, for $${\alpha }_{{\rm{H}}}\, < \,{45}^{\circ }$$, both reversal fields are taken just when the reversible transition have finished and similar dynamic coercive and switching field values are found, which depend on both dH/dt and $${\alpha }_{{\rm{H}}}$$ (see top graph of Fig. 4). In general, the reversal fields increase slowly and logarithmically in dH/dt for low sweep rates (low dynamic regime). For high sweep rates the increase of the reversal field with field sweep rate becomes much faster (high dynamic regime). This behavior has been explained in the literature in terms of a transition between two different thermally activated reversal regimes28,29,30. At low sweep rates the magnetization reverses mainly by domain wall propagation while at higher sweep rates, where the propagation process becomes relatively slow compared to the variation of the applied magnetic field, successive nucleations of reversed domains dominate the reversal. Since the activation energy for domain nucleation is larger than that for domain wall motion, the reversal field varies more strongly with dH/dt in this reversal regime. In addition, in both regimes the dynamic reversal field increases and the rising slope decreases as $${\alpha }_{{\rm{H}}}$$, increases. As a result, the crossover between these two thermally activated regimes is found at higher dH/dt as we move away the e.a. direction.

For $${\alpha }_{{\rm{H}}}\, > \,{45}^{\circ }$$, while the dynamic switching field shows the trend already described, the dynamic coercivity presents a peculiar evolution in which three behaviors for different dH/dt ranges can be distinguished, defining a low, crossover and high dynamical regime regions, respectively (see central graph of Fig. 4). Two of these regions (low and high dynamic regimes) present an approximately linear relationship between $${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$ and $$log$$(dH/dt) but with different slope, which is higher at high dynamic regime. A third region characterized by a dip in $${\mu }_{0}{H}_{{\rm{C}}}$$ is found at the crossover from low dynamic regime to high dynamic regime. Similar behavior was found in epitaxial Fe/GaAs(001) films, where the dip was shifted to lower dH/dt as the temperature was reduced33. It has been suggested that forced depinning from nucleation sites at these sweep rates is responsible for the dip in coercive field, and that there are two distinct timescales associated with the reversal process which correspond to domain nucleation and wall motion, respectively. In our case, this behavior can be simply understood taking into account that for $${\alpha }_{{\rm{H}}}\, > \,{45}^{\circ }$$ the dynamic coercive field can be derived from a still reversible process, happening before the irreversible transition related to the switching field takes place. Therefore, for this angular range, nucleation dynamics cannot be derived from the dynamic coercivity, but from the dynamic switching field. In fact, the latter presents two clear dynamical behaviors following the trend discussed above, i.e., propagative to nucleative regimes. In addition, the crossover between the two regimes still shifts to higher dH/dt values when $${\alpha }_{{\rm{H}}}$$ increases.

Around the h.a. direction, different dynamic $${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$ and $${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$ values are found, as expected from the definition of both reversal fields, which depend on $${\alpha }_{{\rm{H}}}$$. In this angular range the coercivities are taken long before the reversible processes have finished, resulting in a non-dependency of $${\mu }_{{\rm{0}}}{H}_{{\rm{C}}}$$ with dH/dt, and in a decrease as $${\alpha }_{{\rm{H}}}$$ increases, vanishing when approaching the h.a. direction. In turn, $${\mu }_{{\rm{0}}}{H}_{{\rm{S}}}$$ increases as $${\alpha }_{{\rm{H}}}$$ and dH/dt increase. At low dynamic regime the switching field increases, with a maximum at the h.a., and its dynamic slope decreases approaching the h.a. direction. This indicates that the magnetization reversal dynamics close to the h.a. is governed mainly by non-thermally activated rotation processes.

The low dynamic regime of the irreversible transition can be simulated by using a phenomenological model based on thermally activated relaxation “single relaxation time approximation” of propagating magnetic domains walls24,25. The model assumes that the energy barrier for magnetization reversal varies linearly with the applied magnetic field (i.e., domain wall propagation with weak pinning centers) and predicts a logarithmic dependence of the reversal field on the applied sweep rate (equation (7) of28). We want to point out that this analysis has been performed in $${\mu }_{0}{H}_{{\rm{S}}}$$(dH/dt) because the switching field is sensitive just to irreversible processes for the whole angular range. Notice that, although this is also valid for the dynamic coercivity for $${\alpha }_{{\rm{H}}} < {45}^{\circ }$$, it is not correct for larger angles where mixed reversible and irreversible processes are present. The solid lines of Fig. 4 derived from this model reproduce the experimental dynamic evolution for the low dynamic regime. Moreover, the dH/dt validity range of the simulation indicates that the transition from the domain wall propagation regime at lower dH/dt to the domain nucleation regime at higher dH/dt shifts to higher sweep rates as $${\alpha }_{{\rm{H}}}$$ increases (see arrows in Fig. 4). This indicates that the higher irreversible field values found as we move away from the e.a. make nucleation processes more relevant and delay the transition between the dynamic regimes.

The tendency in the high dynamic regime, i.e., where nucleation becomes more relevant during the irreversible transition, can be figured out by simply inspecting the angular dependence evolution of the coercive and switching fields as dH/dt increases. Figure 5 compares the data extracted from the experimental loops (symbols) with the predicted ones by the domain wall pinned (dashed line) model and the Stoner-Wohlfarth (SW) (solid line) models. It is worth noting that the experimental data show a clear transition from a pinned-like behavior at low dH/dt (propagative regime) to a SW-like behavior at high dH/dt (nucleative regime).

The SW model assumes a single particle behavior, i.e., coherent reversal by switching (irreversible process) and/or rotation (reversible) of the whole magnetization, without taking into account any other irreversible magnetization reversal process like nucleation and propagation of magnetic domains. The latter is, in fact, energetically much more favorable in extended systems, in which defects of any kind–structural or morphological–play the main role to activate irreversible magnetic domain nucleation processes at magnetic fields that are significantly lower than expected by the SW model. In fact, low coordination sites such as sample edges, grain boundaries, and topographic roughness, are unavoidable in real samples. These defects can act as pinning centers for the created magnetic domain walls and the reversal subsequently continues via domain wall propagation. In this case, a simple model of pinned 180° magnetic domain walls (pinning model)34 predicts a $$\mathrm{1/|}cos{\alpha }_{{\rm{H}}}|$$ law for the angular dependence of the reversal field, i.e., only the projection of the field along the magnetization is effective. As a consequence coercive field is no longer maximum at the e.a. direction, in clear contrast with the SW model that predicts a maximum value of the coercive field, which is similar to the anisotropy field.

From our dynamic study, at low dH/dt the angular evolution of the irreversible transition shows a pinned-like behavior in a broad angular range around the e.a. direction, In particular, both $${H}_{{\rm{C}}}({\alpha }_{{\rm{H}}})$$ and $${H}_{{\rm{C}}}({\alpha }_{{\rm{H}}})$$ follow the predicted behavior by the pinning model for an angle range $$\pm {60}^{\circ }$$ (see red solid line in Fig. 5(b)). Similar findings have been reported in both perpendicular35 and in-plane36 anisotropy systems, from angular-dependence quasi-static measurements. The experimental data increase as dH/dt increases, but always limited by the expected values from the SW model (see black solid lines in Fig. 5). Remarkably, the similarity between the experimental data at the highest dynamic regime investigated and those predicted by the SW model are very high. Dynamic measurements performed just at the e.a. direction in perpendicular anisotropy systems also showed this tendency, i.e., the coercive field at the e.a. direction becomes closer to the anisotropy field at the fastest dynamical regime37. In addition, we show that the whole angular range of transition fields, including both coercive and switching fields, approaches the SW-like behavior as dH/dt increases (Fig. 5). The transition from the pinned to the SW model with increasing dH/dt can be observed clearly in the polar representation shown in Fig. 1. Thus, our dynamic study shows that pinned-like and SW-like behaviors can be found at low dH/dt and high dH/dt, respectively. Moreover, the data show that this is directly connected with propagative and nucleative regimes, respectively.

The results show that the dynamic properties, including hysteresis, remanences and reversal fields, approach the SW predictions when nucleation processes dominate the magnetization reversal, leading to provide the general trend of the dynamic magnetic properties of other extended magnetic systems. In general, during the irreversible transition the magnetization reverses by nucleation of domains (oriented parallel to the anisotropy axis) and propagation of domain walls. The nucleation sites are associated with defects (or local weakening of the intrinsic anisotropy) and the domain wall propagation is hindered by local pinning centers, as described above. The ratio between the rates of domain wall propagation and nucleation events is highly sensitive to both applied field angle and the applied field sweep rate. Respect to the later, the irreversible transitions become wider as dH/dt increases indicating the presence of a distribution of nucleation energy barriers. In the low dynamic regime, before the crossover, the lowest-energy nucleation barriers are overcome and the domain walls expand driven by the external magnetic field. At high dynamic regime, above the crossover, nucleative processes dominate and both coercivity and switching fields approach the SW predictions as dH/dt increases. At the fastest dH/dt, the whole extended system behaves as a single-like particle because high nucleation rates can inhibit propagative events. Within this general scenario, the crossover between the propagative to nucleative regime would depend strongly on intrinsic properties of the magnetic system, as mentioned below.

### Summary

We have demonstrated not only that a single-particle like magnetic behavior can be found in extended magnetic systems but also for what dynamic conditions, i.e., when nucleative processes govern the reversal. The detailed vectorial-resolved angular-dependent study of a model system, performed over 9 decades of dH/dt and in the whole angular range, provides a general view on the dynamics of magnetization reversal processes. In general, the data show that while thermal activation processes take place during the irreversible transitions, which correspond to nucleation and propagation of magnetic domains, reversible transition via rotation processes are not thermally activated. Propagative and nucleative processes govern the reversal at low dH/dt and high dH/dt, respectively. The transition between both regimes depends on $${\alpha }_{{\rm{H}}}$$, increasing as $${\alpha }_{{\rm{H}}}$$ increases. Dynamical effects are also shown on the angular dependence of the transition fields, where a transition from pinned-like to SW-like behaviors has been found. In particular, the reversal fields behave accordingly to the pinning model for the propagative regime whereas they become closer to the SW model for the nucleative regime, i.e., emerging the Stoner-Wolfhart astroid at dynamic regime as Fig. 1 illustrates.

This study also demonstrates that nucleation processes governing magnetization reversal is at the heart of coercivity enhancement, which is the path for the development of high performance permanent magnets38, as well as it explains why the SW model can describe successfully the angular-dependence properties of more complex extended systems, i.e., exchange biased ferromagnetic/antiferromagnetic bilayers39,40,41,42 and ripple patterned films43, where nucleative processes are much more relevant even in quasi-static conditions. This study emphasizes the importance of dynamical effects in order to understand and control magnetic systems.

## Methods

Detailed description on sample preparation and experimental are described in the Supplementary information. The data presented here correspond to a 20 nm thick Co thin film with well-defined uniaxial magnetic anisotropy. Angular-dependent, time-resolved, vectorial-resolved Kerr magnetometry measurements were performed at room temperature over 9 decades of applied magnetic field sweep rates. With this magnetometry, magnetization reversal dynamics of the two in-plane magnetization components, i.e., parallel ($${M}_{||}$$) and transverse ($${M}_{\perp }$$) to the external applied field has been explored.

The reliability of the dynamical study presented here rests on the accurate dynamic characterization of the time-resolved v-MOKE setup developed, focusing on both electromagnet and detection system. A non-desirable dynamic magnetic response of the electromagnet (i.e., vanishing the linear relationship between the applied current and the induced magnetic field, with opening of the current-field hysteresis loop of the electromagnet) and/or non-timely response (artificial time delay) of the detection system (either from the twin photodiode detector system or the digital oscilloscope) would promote artefacts in the dynamic magnetic measurements. These would display (artificial) magnetic hysteresis loop opening, independently of the applied field angle. The loop opening would provide (wrong) larger reversal fields and remanence values, being the measure more erroneous the higher the applied field sweep rate. In order to avoid this, we have checked that the magnetic field response of the electromagnet is linear with the driving current in the whole dynamic range investigated, i.e., without loop opening, and the rise-time of the detector system has been set to nanosecond timescale. A cross-check, that ensures that both electromagnet and detection system have been properly chosen, comes from the experimental observations of similar dynamic angular-dependent remanence values (see Fig. 3) and non-hysteretic loops at the hard-axis direction in the whole dynamical range investigated (see bottom left graph of Fig. 2).

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## References

1. 1.

J. Stöhr, H. C. Siegmann, Magnetism: From fundamentals to Nanoscale Dynamics (Springer-Verlag, Berlin, 2006).

2. 2.

McCallum, R. W., Lewis, L. H., Skomski, R., Kramer, M. J. & Anderson, I. E. Practical Aspects of Modern and Future Permanent Magnets. Annu. Rev. Mater. Res. 44, 451 (2014).

3. 3.

Albert, F. Origin, development, and future of spintronics. Rev. Mod. Phys. 80, 1517 (2008).

4. 4.

G. Bertotti, Hysteresis in magnetism, Academic Press, (1998)

5. 5.

E. C. Stoner, E. P.Wohlfarth, E. P. (1948). A mechanism of magnetic hysteresis in heterogeneous alloys. Philos. Trans. R. Soc. London, Ser. A 240, 599 (1948); IEEE Trans. Magn. 27, 3475 (1991).

6. 6.

Aharoni, A. A. Theoretical search for domain nucleation. Rev. Mod. Phys. 34, 227–238 (1962).

7. 7.

Vogel, J., Moritz, J. & Fruchart, O. Nucleation of magnetisation reversal, from nanoparticles to bulk materials. C. R. Phys. 7, 977 (2006).

8. 8.

B. D. Cullity, C. D. Graham, Ed. Willey, IEEE Press (2009).

9. 9.

Wernsdorfer, W. Classical and quantum magnetization reversal studied in nanometersized particles and clusters. Adv. Chem. Phys. 118, 99 (2001).

10. 10.

Jamet, M. et al. Magnetic Anisotropy of a Single Cobalt Nanocluster. Phys. Rev. Lett. 86, 4676 (2001).

11. 11.

Wernsdorfer, W. et al. Nucleation of Magnetization Reversal in Individual Nanosized Nickel Wires. Phys. Rev. Lett. 77, 1873 (1996).

12. 12.

J.C. Slonczewski, Theory of Magnetic Hysteresis in Films and Its Application to Computers, IBM Research Memorandum No. 003.111.224 (1956); IEEE Trans. Magn. 45, 8 (2009).

13. 13.

Frei, E. H., Shtrikman, S. & Treves, D. Critical Size and Nucleation Field of Ideal Ferromagnetic Particles. Phys. Rev. 106, 446 (1957).

14. 14.

Ecija, D. et al. Symmetry breaking effects in epitaxial magnetic thin films: Nonsymmetric reversal and butterfly remanence behavior. Phys. Rev. B 77, 024426 (2008).

15. 15.

Perna, P., Mechin, L., Saib, M., Camarero, J. & Flament, S. Imaging the magnetization reversal of step-induced uniaxial magnetic anisotropy in vicinal epitaxial La0.Sr0MnO3 films. New Journal of Physics 12, 103033 (2011).

16. 16.

Camarero, J. et al. Origin of the asymmetric magnetization reversal behavior in exchange-biased systems: Competing anisotropies. Phys Rev. Lett. 95, 057204 (2005).

17. 17.

Bonfim, M. et al. Element-Selective Nanosecond Magnetization Dynamics in Magnetic Heterostructures. Phys. Rev. Lett. 86, 3646 (2001).

18. 18.

W. F. Brown, M (Wiley, N York, 1963).

19. 19.

Sun, J. et al. Thermal activation-induced sweep-rate dependence of magnetic switching astroid. Appl. Phys. Lett. 78, 4004 (2001).

20. 20.

Jiménez, E. et al. Vectorial Kerr magnetometer for simultaneous and quantitative measurements of the in-plane magnetization components. Rev. Sci. Instrum. 85, 053904 (2014).

21. 21.

Cuñado, J. L. F. et al. Vectorial-magneto optical Kerr effect technique combined with variable temperature and full angular range all in a single setup. Rev. Sci. Instrum. 86, 046109 (2015).

22. 22.

J. Miltat, G. Albuquerque, A. Thiaville, In: B. Hillebrands, K. Ounadjela (Eds.), Spin Dynamics in Confined Magnetic Systems I, In: Topics in Appl. Phys., vol. 83 (Springer-Verlag, Berlin, 2002).

23. 23.

Moore, T. A. & Bland, J. A. C. Mesofrequency dynamic hysteresis in thin ferromagnetic films. J. Phys.: Condens. Matter. 16, R1369 (2004).

24. 24.

Bruno, P. et al. Hysteresis properties of ultrathin ferromagnetic films. J. Appl. Phys. 68, 5759 (1990).

25. 25.

Raquet, B. et al. Dynamical properties of magnetization reversal in an ultrathin AuCo film. J. Magn. Magn. Mater. 150, L5–L12 (1995).

26. 26.

Moore, T. A., Rothman, J., Xu, Y. B. & Bland, J. A. C. Thickness-dependent dynamic hysteresis scaling behavior in epitaxial Fe/GaAs(001) and Fe/InAs(001) ultrathin films. J. Appl.Phys. 89, 7018 (2001).

27. 27.

Moore, T. A., Walker, M. J., Middleton, A. S. & Bland, J. A. C. Mesofrequency switching dynamics in epitaxial CoFe and Fe thin films on GaAs(001). J. Appl. Phys. 97, 053903 (2005).

28. 28.

Raquet, B., Mamy, R. & Ousset, J. C. Magnetization reversal dynamics in ultrathin magnetic layers - Au/Co/Au sandwiches. Phys. Rev. B 54, 4128 (1996).

29. 29.

Camarero, J. et al. Dynamical properties of magnetization reversal in exchange-coupled NiO/Co bilayers. Phys. Rev. B 64, 172402 (2001).

30. 30.

Camarero, J., Pennec, Y., Bonfim, M., Vogel, J., Pizzini, S., Fontaine, A., Cartier, M., Fettar, F. & Dieny, B. Magnetization reversal dynamics in exchange-coupled NiO/Co bilayers. J. Appl. Phys. 89, 6585 (2001).

31. 31.

Garcia, F. et al. Exchange bias with perpendicular anisotropy in (Pt-Co)/sub n/-FeMn multilayers. IEEE Transactions on Magnetics 38, 2730 (2002).

32. 32.

Pennec, Y. et al. Switching-mode-dependent magnetic interlayer coupling strength in spin valves and magnetic tunnel junctions. Phys. Rev. B 69, 180402 (2004).

33. 33.

Moore, T. A., Wastlbauer, G. & Bland, J. A. C. Thermally activated and field sweep rate-dependent switching in epitaxial Fe/GaAs(001). J. Phys.: Condens. Matter 15, 407 (2003).

34. 34.

S. Chikazumi, Physics of Ferromagnetism, Oxford Science Publications, New York (1997), pp. 118–119, pp. 491.

35. 35.

Givord, D., Tanaud, P. & Viadieu, T. Angular dependence of coercivity in sintered magnets. J. Magn. Magn. Mater. 72, 247 (1988).

36. 36.

Perna, P. et al. Tailoring magnetic anisotropy in epitaxial half metallic La 0.Sr 0.MnO3 thin films. Appl. Phys. 110, 1391 (2011).

37. 37.

Moritz, J. et al. Experimental evidence of a 1/H activation law in nanostructures with perpendicular magnetic anisotropy. Phys. Rev. B 71, 100402 (2005).

38. 38.

Skomski, R. et al. Predicting the Future of Permanent-Magnet Materials. IEEE Trans. Magn. 49(No. 7), 3215 (2013).

39. 39.

Jiménez, E. et al. Emergence of noncollinear anisotropies from interfacial magnetic frustration in exchange-bias systems. Phys. Rev. B 80, 014415 (2009).

40. 40.

Jiménez, E. et al. Highly asymmetric magnetic behavior in exchange biased systems induced by noncollinear field cooling. Appl. Phys. Lett. 95, 122508 (2009).

41. 41.

Jiménez, E. et al. Role of anisotropy configuration in exchange-biased systems. J. Appl. Phys. 109, 07D730 (2011).

42. 42.

Perna, P. et al. Interfacial exchange-coupling induced chiral symmetry breaking of spin-orbit effects. Phys. Rev. B 92, 220422 (2015).

43. 43.

Colino, J. M., Arranz, M. A., Barbero, A. J., Bollero, A. & Camarero, J. Surface magnetization and the role of pattern defects in various types of ripple patterned films. J. Phys. D: Appl. Phys. 49, 135002 (2016).

## Acknowledgements

We thank the research support services of UAM (SEGAINVEX) for the development of the v-MOKE detectors and power supplies. This work has been supported by MINECO (Ministerio de Economía y Competitividad) through Projects No. MAT2012-39308, FIS2015-67287-P, and FIS2016-78591-C3-1-R, by the Comunidad de Madrid through Project S2013/MIT-2850 NANOFRONTMAG-CM, and by MINECO through the FLAG-ERA Programme of Graphene Flagship: SOgraph project (No. PCIN-2015-216); and M-era.Net Programme: NEXMAG project (PCIN- 2015-126). IMDEA-Nanociencia acknowledges support from the ‘Severo Ochoa’ Program for Centres of Excellence in R&D (MINECO, Grant SEV-2016-0686). P.P. acknowledges support through the Marie Curie AMAROUT EU Programme and JCI-2011-09602. A.B. acknowledges MINECO through the ENMA-National project (MAT2014-56955-R).

## Author information

J.L.F.C, A.B., T.P-C., R. M., and J.C. conceived and designed the experiments. T.P-C. and A. M. carried out the first dynamic measurements which were completed by J.L.F.C. and P.P., with the assistance of A.B. and J.C. Static measurements were performed by J.L.F.C. and J.P. The dynamic v-MOKE instrument was developed by J.C., A.B., P.P., F.T, R.G., and D.C. Samples were grown by F.A. and A.G. with the assistance of M.A.N. Numerical simulations were carried out by J.L.F.C. and J.C. All authors discussed the data and commented on the manuscript.

### Competing Interests

The authors declare that they have no competing interests.

Correspondence to José Luis F. Cuñado or Julio Camarero.