Anomalous Nernst effect in stressed magnetostrictive film grown onto flexible substrate

The anomalous Nernst effect in nanostructured magnetic materials is a key phenomenon to optimally control and employ the internal energy dissipated in electronic devices, being dependent on, for instance, the magnetic anisotropy of the active element. Thereby, here, we report a theoretical and experimental investigation of the magnetic properties and anomalous Nernst effect in a flexible magnetostrictive film with induced uniaxial magnetic anisotropy and under external stress. Specifically, we calculate the magnetization behavior and the thermoelectric voltage response from a theoretical approach for a planar geometry, with magnetic free energy density that takes into account the induced uniaxial and magnetoelastic anisotropy contributions. Experimentally, we verify modifications of the effective magnetic anisotropy by changing the external stress, and explore the anomalous Nernst effect, a powerful tool to investigate the magnetic properties of magnetostrictive materials. We find quantitative agreement between experiment and numerical calculations, thus elucidating the magnetic behavior and thermoelectric voltage response. Besides, we provide evidence to confirm the validity of the theoretical approach to describe the magnetic properties and anomalous Nernst effect in ferromagnetic magnetostrictive films having uniaxial magnetic anisotropy and submitted to external stress. Hence, the results place flexible magnetostrictive systems as promising candidates for active elements in functionalized touch electronic devices.

New and more efficient ways to make use the internal energy converted into heat in electronic devices are of crucial importance for a sustainable future 1,2 . In this field, the engineering of magnetostrictive films onto flexible substrates is an exciting area of research with potential to the development of energy-efficient technologies, covering the impacts of the external stress on the quasi-static and dynamic magnetic properties [3][4][5][6] . Specifically, the interplay of magnetostrictive and temperature effects provides us a playground to the investigation of fundamental anisotropic magnetothermoelectric effects, for instance, the spin polarization dependence of the thermoelectric energy [7][8][9][10] .
In magnetic materials, the thermoelectric voltage, defined as the direct conversion of the temperature gradient to electrical voltage, is investigated through thermomagnetic phenomena, such as the spin Seebeck effect (SSE) and the anomalous Nernst effect (ANE) 11,12 . Both of them essentially consist in the application of a magnetic field and a temperature gradient, thus generating an electric field → E . Specifically, for the anomalous Nernst effect in nanostructured magnetic materials, an electric field → E ANE is induced by the interplay of the magnetization → m and the temperature gradient ∇T, being a result of → ∝ → × ∇ E m T ANE . Thus, given that the corresponding thermoelectric voltage V ANE in magnetic materials is observable even with small thermal gradients at room temperature, ANE becomes a key effect to optimally control and employ the internal energy dissipated in electronic devices. In the near past, ANE has been extensively investigated, disclosing that V ANE is strongly dependent on the crystallographic orientation in magnetic materials 13 , type of material (for instance, Fe and Ni have ANE coefficient with opposite signs), thickness of the layers in the film geometry 12,14 , and magnetic anisotropy 15 . However, despite the recent advances in this field, there still are several aspects related to the anomalous Nernst effect in nanostructured ferromagnetic materials that are not yet fully understood or explored. Among the different investigated ferromagnets, materials with high-spin polarization are the main elected to constitute spintronics devices. In this context, CoFeB alloys in the film geometry arise as one of the most promising candidates for this kind of application due to their magnetic properties, such as high permeability, high saturation magnetization, low coercive field, and well-defined magnetic anisotropy [16][17][18][19] . These features place the CoFeB alloys suitable to the production of, for instance, magnetic tunnel junctions with high magnetoresistance [20][21][22][23] and spin-transfer torque 23 , as well as to the investigation of a sort of phenomena, as spin pumping 24,25 , spin Hall effect 26 , and inverse spin Seebeck effect 27 . It is known that the magnetic properties of CoFeB films are strongly dependent on the thickness [28][29][30] . Films thinner than 5 nm usually exhibit strong perpendicular magnetic anisotropy (PMA) 28 , while the thicker ones commonly show in-plane magnetic anisotropy 29,30 . Moreover, due to its magnetostrictive properties, thick-CoFeB films have been grown onto flexible substrates, thus becoming essential systems to investigate the influence of the stress on the effective magnetic anisotropy 16,17 , as well as appearing as promising materials for application in flexible magnetic devices 31 , disposable electronics, smart cards, light-emitting diodes, wearable electronics and a broad range of sensors 18,[32][33][34][35] .
To pave the way, looking for effective integration between the thermoelectric voltage experiments and flexible spintronic devices, the anomalous Nernst effect emerges as a powerful tool to explore thermoelectric effects in samples with magnetostrictive properties. In this work, we perform a theoretical and experimental investigation of the magnetic properties and anomalous Nernst effect in a flexible magnetostrictive film with induced uniaxial magnetic anisotropy and under external stress. Specifically, from the theoretical approach, we calculate the magnetization behavior and the thermoelectric voltage response; experimentally, we verify modifications of the effective magnetic anisotropy in stressed samples through thermoelectric voltage measurements, and explore the anomalous Nernst effect as an efficient way to study flexible magnetostrictive film by modifying both, the magnetic field and external stress. We find quantitative agreement between experiment and numerical calculations, thus elucidating the magnetic properties and thermoelectric voltage response. Besides, we provide evidence to confirm the validity of the theoretical approach to describe the magnetic properties and anomalous Nernst effect in ferromagnetic magnetostrictive films having uniaxial magnetic anisotropy and submitted to external stress.

Results
Theoretical approach. Here, we focus on a ferromagnetic magnetostrictive film with uniaxial magnetic anisotropy, which is submitted to external stress; and we model it as a planar system, as illustrated in Fig. 1.
In the anomalous Nernst effect in magnetic materials, an electric field → E ANE is induced by the interplay of the magnetization → m of the sample and a temperature gradient ∇T; and the relationship between these quantities can be expressed as Figure 1. Schematic configuration of our theoretical system-a ferromagnetic magnetostrictive film with uniaxial magnetic anisotropy, which is submitted to external stress. (a) Anomalous Nernst effect in a film. In our numerical calculation, while the magnetization → m lies in the film plane, the temperature gradient ∇T is normal to the plane. The electric field associated with the anomalous Nernst effect is a result of , and thus the thermoelectric voltage V ANE is proportional to a component of → E ANE , given that its detection is performed with electrical contacts at the ends of the main axis of the film. (b) Definitions of the vectors and angles employed in the numerical calculations of magnetization and thermoelectric voltage. Here, we consider the magnetization vector → m , whose orientation for each given magnetic field value is set by θ m and φ m , the equilibrium angles with respect to the z and x axes (this latter is also represented by the dashed line above the film), respectively. In particular, due to the film geometry and system thickness, here θ m is constant and equal to 90°. The magnetic field is kept in the film plane, i.e. θ =  90 H , although its orientation can be modified by varying ϕ H from 0° up to 360°, having as reference the dashed line indicated in the illustration. The unit vector û k , not shown here, is defined by θ k and φ k , and indicates the direction of the uniaxial magnetic anisotropy induced during deposition; σ u is given by θ = σ  90 and ϕ = σ  90 , and describes the direction of the magnetoelastic anisotropy induced by the stress applied to the sample during the experiment; and û eff , not shown here too, is described by θ u eff and ϕ u eff , and represents the orientation of the effective magnetic anisotropy, a result of the competition between the contributions of the induced uniaxial and magnetoelastic anisotropies. The unit vector normal to the film plane, also not shown, is along the z direction, i.e. =n k. Finally, for the thermoelectric voltage calculation, the temperature gradient ∇T is normal to the film plane. Further, the V ANE detection is performed with electrical contacts at the ends of the main axis of the film.
s ; λ N is the anomalous Nernst coefficient, μ o is the vacuum magnetic permeability, and m s is the saturation magnetization of the ferromagnetic alloy, which is oriented along to the unit vector . m In our theoretical approach, we consider a typical ANE experiment in a film, in which the temperature gradient is normal to the film plane, while the magnetization lies in the plane, as depicted in Fig. 1(a). The corresponding thermoelectric voltage V ANE , detected by electrical contacts at the ends of the main axis of the film, is thus given by where the integration limits are set by the distance between the electrical contacts, which in our case is L. As a result, the measured V ANE is proportional to the → E ANE component along to the direction defined by the contacts, as we can see in Fig. 1(a,b).
For films under an out-of-plane temperature gradient, S N can be experimentally estimated through N ANE where t f is the film thickness, L is the own distance between the probe electrical contacts in the experiment, ΔT f is the temperature variation across the film (see Methods for details on the ΔT f estimation and its relation with the temperature variation ΔT measured experimentally across the sample), and V ANE S max is a very particular maximum V ANE value that we set from experiment. Specifically, this latter is obtained when the sample is magnetically saturated, with → m in the film plane and transverse to the detection direction defined by the electrical contacts; this configuration yields → E ANE parallel to the direction of the voltage detection, having its highest magnitude. After all, our theoretical approach provides a normalized V ANE response, which is rescaled using an experimental S N value (see Methods for details on the S N estimation) for comparison.
The theoretical system and the definitions of the vectors considered to perform the numerical calculations are depicted in Fig. 1(b). Looking at the thermoelectric voltage at a constant in-plane magnetic field that is high enough to keep the film magnetically saturated, the magnetization follows the orientation of the magnetic field, i.e. ϕ ϕ = m H . As consequence, the angular dependence of V ANE with the magnetic field is considerable simplified, On the other hand, it is worth remarking that the amplitude and direction of the magnetization may be changed by the application of a magnetic field → H and/or external stress σ, thus modifying → E ANE and, consequently, V ANE . At the non-saturated magnetic regime, the equilibrium angle ϕ m of the magnetization is a result of the competition between the applied magnetic field and the magnetic anisotropies of the sample, leading to a complex dependence of the V ANE with the magnetic field. To investigate the magnetic properties and thermoelectric voltage response of magnetostrictive films with induced uniaxial magnetic anisotropy, we employ a modified Stoner-Wohlfarth model 36 . Here, we consider the magnetic free energy density as where → m is the magnetization vector of the ferromagnetic layer, m is its corresponding versor, m s is the saturation magnetization, = H K m 2 / k u s is the anisotropy field, where K u is the induced uniaxial magnetic anisotropy constant, λ s is the saturation magnetostriction constant, σ is the applied stress, and n is the versor normal to the film plane. The first term of the magnetic free energy density indicates the Zeeman interaction, the second one is the demagnetizing energy density, and the third term is associated to the induced uniaxial magnetic anisotropy oriented along û k . Finally, the fourth term describes the magnetoelastic energy density for an elastically medium with isotropic magnetostriction. This latter term relates the saturation magnetostriction constant λ s and the stress σ applied to the system, and gives rise to the magnetoelastic anisotropy contribution along σ u . In particular, the product between λ s and σ modifies the effective magnetic anisotropy of the sample. While for λ σ>0 s a magnetoelastic anisotropy axis is induced along the same direction of the applied stress, for λ σ<0 s , this magnetoelastic anisotropy axis is oriented perpendicularly to the direction of the stress [36][37][38] .
From the appropriate magnetic free energy density, a routine for the energy minimization determines the equilibrium angles θ m and ϕ m of the magnetization at a given magnetic field → H , and we calculate the normalized magnetization m m / s and the thermoelectric voltage V ANE curves. First of all, to confirm the validity of our theoretical approach, we consider a system consisting of a film with uniaxial magnetic anisotropy and without stress, i.e. σ=0 MPa. For the numerical calculations, we take into account the following system parameters:  Figure 2(a), in which we show the magnetization calculation for distinct ϕ H values, uncovers the expected dependence of the magnetization curves with the orientation between the easy magnetization axis and magnetic field, disclosing all the traditional features of uniaxial magnetic systems 41 . Given that φ =  5 k , the curve for ϕ =  0 H reveals the signatures of a typical easy magnetization axis. Specifically, the magnetization loop presents normalized remanent magnetization ∼1 and coercive field of around 35 Oe, this latter close to H k . For the magnetization curve at ϕ =  90 H in turn, the normalized remanent magnetization reduces to ∼0.08 and the coercive field to around 2 Oe, values compatible with a hard magnetization axis. Remarkably, the small deviation of ϕ k yields an hysteretic behavior for ϕ =  90 H , giving rise to a typical hard axis behavior with a non-zero coercive field. Regarding the thermoelectric voltage calculation, Fig. 2(b) shows the V ANE response, with Δ = T 27 K, as a function of the magnetic field for distinct ϕ H values. Notice the quite-interesting evolution in the shape of the curves as the magnitude and orientation of the field are altered. It is noteworthy that the V ANE detection is performed with electrical contacts at the ends of the main axis of the film, and here this direction is almost transverse to û k , which defines the orientation of the induced uniaxial magnetic anisotropy. At small ϕ H values, the V ANE curves seem to mirror the magnetization loops. This feature is a signature that the magnetization is kept close to the easy magnetization axis, thus favoring the alignment between → E ANE and the detection direction defined by the electrical contacts. Therefore, V ANE is directly proportional to the magnitude of the magnetization. On the other hand, as the ϕ H value increases and the field is not nearby the easy magnetization axis, the V ANE curves lose the www.nature.com/scientificreports www.nature.com/scientificreports/ square shape. This fact is a consequence of the competition between two energy terms, the first associated with the Zeeman interaction and the second one related to the induced uniaxial magnetic anisotropy. At the low magnetic field range, the magnetization remains close to the easy magnetization axis, leading to high V ANE values. However, as the magnetic field increases, the Zeeman energy term dominates, and the magnetization rotates out from the easy axis, following the field. As a result, the → E ANE component along the detection direction defined by the electrical contacts decreases and V ANE is drastically reduced. Figure 2(c) presents the V ANE values, at = ± H 300 Oe and with ∆ = T 27 K, as a function of ϕ H . At these field values, our system is magnetically saturated, in a sense that the magnetization follows the orientation of the magnetic field. As expected, the curves draw a clear dependence of V ANE with the sign of the magnetic field and primarily with ϕ H , this latter evidenced by a well-defined cosine shape, as described in Eq. (4).
Further, Fig. 2(d) shows the V ANE behavior as a function of ϕ H at = + H 300 Oe for selected ∆T values. In this case, although the amplitude of the curves is altered, the angular dependence is kept constant, also corroborating Eq. (4). At this magnetic saturation state, the maximum V ANE value is found for ϕ =  0 H , and corresponds to V ANE Smax , according to our setup illustrated in Fig. 1(a,b). Moreover, a linear dependence of V ANE Smax with ∆T is obtained, as we can see in the inset of Fig. 2(d).
After all, the numerical calculations obtained with our theoretical approach provide us an overview of the ANE for a nanostructured system consisting of a film with induced uniaxial magnetic anisotropy. From now, to go beyond, the main challenge to the description of different systems resides in the appropriate writing of the magnetic free energy density.
Comparison with the experiment. The previous calculations have qualitatively described the main features of the magnetic behavior and thermoelectric voltage response in a film with uniaxial magnetic anisotropy and without stress.
From now on, we investigate the quasi-static magnetic properties and anomalous Nernst effect in a Co 40 Fe 40 B 20 (from now on called CoFeB) film with thickness of 300 nm grown onto a flexible (Kapton ® ) substrate (see Methods for details on the film deposition and experiments). In this context, we perform experiments for the sample with and without external stress. Figure 3 shows experimental results of the magnetic response and the thermoelectric voltage for the CoFeB film without stress. Figure 3(a), in which we present the magnetization response for the film grown onto a flexible substrate as a function of the magnetic field for distinct ϕ H values, discloses curves that assign the characteristic behavior of a system with uniaxial magnetic anisotropy close to the direction perpendicular to the main axis of the sample. While coercive field of ∼42 Oe and normalized remanent magnetization of ∼1 are found for ϕ =  Regarding the thermoelectric voltage results, Fig. 3(b) shows the V ANE response for the film grown onto a flexible substrate, with Δ = T 27 K, as a function of the magnetic field for distinct ϕ H values. The experimental V ANE curves are also in concordance with the numerical calculations presented in Fig. 2(b), reflecting all features of systems with uniaxial magnetic anisotropy and without external stress. Specifically, we find here the evolution in the shape of the curves as the magnitude and orientation of the field are altered. Moreover, at high magnetic field values, when the film is magnetically saturated, we verify the angular dependence of V ANE , having μ ≈ V 20

ANE Smax
V, and the characteristic reduction of its value to zero as ϕ H increases to 90°. However, at the low field range, it is noteworthy that a discrepancy between theory and experiment may be found. In particular, as ϕ H is raised to 90°, V ANE does not reach the expected maximum of 20 μV found at ϕ =  0 H , a value also evidenced www.nature.com/scientificreports www.nature.com/scientificreports/ numerically in Fig. 2(b). This divergence is primarily associated with the magnetization process at low magnetic fields and to the existence of magnetic domains in the film, a fact that is not taken into account in our microspin modified Stoner-Wohlfarth theoretical approach. Indeed, the magnitude of the magnetization in the experiment is not kept constant at the low-field levels, leading to a reduction of the V ANE value.
From the experimental results found for the flexible film, shown in Fig. 3 and compared with the calculated ones presented in Fig. 2, we corroborate the angular dependence of the magnetization and thermoelectric voltage curves in films with uniaxial magnetic anisotropy. Going beyond, from now on, we focus our efforts on the magnetic response and thermoelectric voltage in a magnetostrictive system under stress. As aforementioned, CoFeB alloy has high saturation magnetostriction constant, reaching λ ≈ + . × − 30 0 10 s 619,40 . Therefore, we are able to manipulate here the magnetic properties, i.e. the effective magnetic anisotropy, of our magnetostrictive CoFeB film grown onto a flexible substrate through the application of stress.  Fig. 4(a), we uncover the modifications of the effective magnetic anisotropy with the stress level. Specifically, while the effective anisotropy is well-described by ϕ k eff roughly close to ϕ k for σ = 0, the changes in the coercive field, remanent magnetization, as well as the own shape of the magnetization curves as the stress level increases are straight consequences of the raise of the magnetoelastic anisotropy contribution to the effective magnetic anisotropy. This raise leads to changes in the orientation û k eff of the effective magnetic anisotropy with the increase of the stress value, thus modifying the whole magnetic behavior and magnetization curves. For σ = 700 MPa, the square curve with smaller coercive field reveals an intermediate magnetic behavior. It arise from an effective magnetic anisotropy that is still roughly close to the direction of the magnetic field at ϕ =  0 H , but has a significant component along the main axis of the sample due to the magnetoelastic contribution.

. From the magnetization response shown in
However, for σ = 1400 MPa, the stress is high enough to set the effective magnetic anisotropy axis close to σ u , i.e. ≈  u 90 eff . Consequently, as expected, the magnetization curve at ϕ =  0 H has fingerprints of a hard magnetization axis, with non-zero values for coercive field and normalized remanent magnetization due to anisotropy dispersion. Therefore, the whole magnetic behavior of the flexible magnetostrictive film under stress is a result of the competition between the induced uniaxial magnetic anisotropy and the magnetoelastic anisotropy contribution. As a consequence, this competition allows us to tailor the effective magnetic anisotropy and, consequently, the anomalous Nernst effect. Remarkably, as we can confirm from Fig. 4(b), modifications in the V ANE response are already visible at ϕ =  0 H , when just the stress is altered in an experimental manner. The most striking experimental and theoretical findings here are shown in Fig. 5, which discloses the evolution of the V ANE response with the ϕ H and stress σ for the CoFeB film grown onto a flexible substrate. The numerical calculations for a film with uniaxial magnetic anisotropy and under stress are performed considering parameters similar to those previously employed in Fig. 2  www.nature.com/scientificreports www.nature.com/scientificreports/ . × − 1 14 10 5 and . × − 1 09 10 5 V/K (see Methods for details on the S N estimation) for the calculations with σ = 0, 700, and 1400 MPa, respectively. In particular, the decrease of S N with σ is straightly verified through the reduction of the V ANE Smax ; and we associate it to modifications in the energy relaxation time close of the Fermi level, which can be altered by the stress application 42 . Then, notice the striking agreement between our experiments and numerical calculations, including three important features: the own shape of the V ANE curves, the ϕ H dependence of the evolution in the shape of the curves, and amplitude of the V ANE response at high magnetic fields, i.e. at the magnetic saturation state.
From Fig. 5(a), the V ANE curves for the film without stress exhibit all the features found for a film with uniaxial magnetic anisotropy, as expected; hence, their interpretation is the very same to that previously reported for Fig. 2(b) and 3(a.II,b.II). With respect to the shape of the curves and its evolution with the orientation of the magnetic field, it is worth observing that the V ANE response pattern changes with ϕ H crossing over through ϕ k eff . Specifically, keeping in mind that in this case the effective magnetic anisotropy orientation û k eff is the own uniaxial magnetic anisotropy direction û k with ϕ ≈  30 k , the V ANE curves for ϕ ϕ < H k eff have shape mirroring the corresponding magnetization loops presented in Fig. 4(a). At small ϕ H values, represented in Fig. 5(a) by the curve for ϕ =  0 H , the magnetization is kept close to the magnetic field direction and/or to the easy magnetization axis. It favours the alignment between → E ANE and the detection direction defined by the electrical contacts, and therefore V ANE is directly proportional to the magnitude of the magnetization. The V ANE response for ϕ ϕ > H k eff www.nature.com/scientificreports www.nature.com/scientificreports/ in turn, depicted by ϕ =  40 H and 70°, discloses curves with completely different signatures, which lose the square shape. For these cases, at high magnetic field values, the magnetization is aligned with the field and, consequently, V ANE is drastically reduced; at the low magnetic field range, the magnetization → m rotates and remains close to the easy magnetization axis û eff , as we can see in the schematic representation in Fig. 5(a.III), leading to higher V ANE values.
For the film under σ ≈ 700 MPa, Fig. 5(b) shows curves with a slightly different profile. In this case, the effective magnetic anisotropy is described by an angle ϕ k eff that lies between 40° and 70°, in a sense that the change in the V ANE response pattern takes place within this angular range. Hence, observe that the V ANE responses at ϕ =  0 H and 40° have the features of a magnetization curve, just presenting a decrease in the amplitude of the V ANE signal at the magnetic saturation state, as expected due to the thermoelectric voltage configuration in the experiment. At ϕ =  70 H , the shape of the V ANE curves considerably, suggesting the competition between the Zeeman interaction and the effective magnetic anisotropy. In this case, at high fields, the magnetization follows the magnetic field, leading to a decrease of V ANE . However, as the field decreases, the Zeeman interaction is reduced and the magnetization → m turns to û eff . As a consequence, there is the increase in the → E ANE component along the V ANE detection direction, as we can see in the schematic representation in Fig. 5(b.III). Obviously, as aforementioned, the discrepancy between experiment and theory at this low-field values is primarily associated with the magnetization process and to the existence of magnetic domains in the film, which is not taken into account in our theoretical approach, as already discussed.
At last, for the film under σ ≈ 1400 MPa shown in Fig. 5 Fig. 4(a). As ϕ H increases, we find the decrease in the amplitude of the V ANE signal at the magnetic saturation state, as expected. Once the magnetic field decreases, irrespective of ϕ H , the magnetization → m rotates to the orientation û eff of the effective magnetic anisotropy. Given that → E ANE tends to be almost transverse to the V ANE detection direction, as we can confirm through the schematic representation in Fig. 5(c.III), a decrease in the V ANE value is also found at low field values and, as a consequence, the evolution in the shape of the V ANE curves is not observed here. In particular, for ϕ =  90 for the whole magnetic field range. Finally, looking at the angular dependence of the V ANE signal amplitude at a given magnetic field, Fig. 6 shows the thermoelectric voltage as a function of ϕ H for the CoFeB film under selected stress levels. In Fig. 6(a), the sample is magnetically saturated, irrespective on the stress level. As a consequence, the V ANE response is precisely the one described by Eq. (4), with a well-defined cosine shape. Another important test of consistency of our approach is also given by the V ANE behavior at non-saturated states. The curves are a result of the competition between the uniaxial magnetic anisotropy and the magnetoelastic anisotropy, leading to considerable changes in the shape and amplitude of the V ANE response. Notice the striking quantitative agreement between experiment and theory in Fig. 6(b).
Hence, we are able to describe through numerical calculations all the main features of the V ANE response. Thus, we provide experimental evidence to confirm the validity of the theoretical approach to describe the magnetic properties and anomalous Nernst effect in ferromagnetic magnetostrictive films with uniaxial magnetic anisotropy and submitted to external stress.

Discussion
In summary, we have performed a theoretical and experimental investigation of the magnetic properties and anomalous Nernst effect in a flexible magnetostrictive film with induced uniaxial magnetic anisotropy and under external stress. Our findings have raised numerous interesting issues on the anomalous Nernst effect in nanostructured magnetic materials. In particular, they have shown how the magnetization behavior and the thermoelectric voltage response evolve with both, the magnetic field and external stress. Hence, by comparing our experiments with numerical calculations, we have elucidated the magnetic properties and thermoelectric voltage and demonstrated the possibility of tailoring the anomalous Nernst effect in a flexible magnetostrictive film. The quantitative agreement between experiment and numerical calculations has provided us evidence to confirm the validity of the theoretical approach to describe the magnetic properties and anomalous Nernst effect in ferromagnetic magnetostrictive films with uniaxial magnetic anisotropy and submitted to external stress. The results place flexible magnetostrictive systems as promising candidates for active elements in functionalized touch electronic devices.

Methods
Estimation of ΔT f . The relation between the temperature variation ΔT measured experimentally across the sample and the effective temperature variation ΔT f in the film is given by 43  Fig. 7. In par-www.nature.com/scientificreports www.nature.com/scientificreports/  www.nature.com/scientificreports www.nature.com/scientificreports/ ticular, ΔT f is calculated by using Eq. (6) and thus S N is given by Eq. (3). As a result, we assume = . × − S 1 31 10 N 5 , . × − 1 14 10 5 and . × − 1 09 10 5 V/K for the calculations with σ = 0, 700, and 1400 MPa, respectively. Here, it is worth mentioning that the estimated S N values may be different from the actual ones, given that the measured ΔT can include the parasitic contribution due to the interfacial thermal resistance between the sample and the heat sink.
Sample preparation. We investigate the anomalous Nernst effect in a Co 40 Fe 40 B 20 (CoFeB) film with thickness of 300 nm grown onto a flexible (Kapton ® ) substrate. The film is deposited by magnetron sputtering onto a substrate with dimensions of 10 × 6 mm 2 . The deposition process is carried out with the following parameters: base pressure of 5 × 10 −6 Torr, deposition pressure of 3.0 × 10 −3 torr with a 99.99% pure Ar at 50 sccm constant flow, and with 50 W set in the DC source. By using these parameters, the deposition rate is 1.86 nm/s. During the deposition, a constant in-plane magnetic field of 1 kOe is applied perpendicularly to the main axis of the substrate in order to induce an uniaxial magnetic anisotropy.
Magnetization measurements. Quasi-static magnetization curves are obtained within the range between ϕ =  0 H (perpendicular) and ϕ =  90 H (along the main axis of the film), in order to verify the magnetic properties. The curves are acquired at room temperature using a Lake Shore model 7404 vibrating sample magnetometer, with maximum in-plane magnetic field of ±300 Oe.
Thermoelectric voltage experiments. We employ a homemade experimental system to measure the thermoelectric voltage associated with the anomalous Nernst effect. In our experimental setup, the temperature gradient ∇T is normal to the film plane. A Peltier module is used to heat or cool the top of the sample while the substrate is kept in thermal contact with a heat sink, a copper block at room temperature. The temperature difference ΔT across the sample (film and Kapton substrate) is measured with a differential micro-thermocouple, depicted in Fig. 8. The magnetic field is kept in the film plane, although its orientation can be modified by varying ϕ H from 0° up to 360°, having as reference the dashed line indicated in Fig. 1(b). Finally, the V ANE detection is performed using a nanovoltmeter with electrical contacts at the ends of the main axis of the film, also illustrated in Fig. 1(a,b), whose separation distance is = .

Stress application.
The magnetization measurements and thermoelectric voltage experiments are carried out in a CoFeB film grown onto a flexible substrate. In this context, we perform acquisitions for the sample with and without stress. The stress is applied by bending the sample, along the main axis, during the measurement. In particular, Kapton strips are inserted under the film substrate in order to induce the bending, as illustrated in Fig. 8. The magnitude of the stress σ is calculated following the procedure previously employed in refs 36,38 . By bending the flexible substrate, we are able to induce tensile stress in the film, thus modifying the effective magnetic anisotropy 38,47,48 .