Skip to main content

Thank you for visiting You are using a browser version with limited support for CSS. To obtain the best experience, we recommend you use a more up to date browser (or turn off compatibility mode in Internet Explorer). In the meantime, to ensure continued support, we are displaying the site without styles and JavaScript.

Unravelling and controlling hidden imprint fields in ferroelectric capacitors


Ferroelectric materials have a spontaneous polarization that can point along energetically equivalent, opposite directions. However, when ferroelectric layers are sandwiched between different metallic electrodes, asymmetric electrostatic boundary conditions may induce the appearance of an electric field (imprint field, Eimp) that breaks the degeneracy of the polarization directions, favouring one of them. This has dramatic consequences on functionality of ferroelectric-based devices such as ferroelectric memories or photodetectors. Therefore, to cancel out the Eimp, ferroelectric components are commonly built using symmetric contact configuration. Indeed, in this symmetric contact configuration, when measurements are done under time-varying electric fields of relatively low frequency, an archetypical symmetric single-step switching process is observed, indicating Eimp ≈ 0. However, we report here on the discovery that when measurements are performed at high frequency, a well-defined double-step switching is observed, indicating the presence of Eimp. We argue that this frequency dependence originates from short-living head-to-head or tail-to-tail ferroelectric capacitors in the device. We demonstrate that we can modulate Eimp and the life-time of head-to-head or tail-to-tail polarization configurations by adjusting the polarization screening charges by suitable illumination. These findings are of relevance to understand the effects of internal electric fields on pivotal ferroelectric properties, such as memory retention and photoresponse.


Ferroelectric materials are receiving an enormous attention due to a plethora of already real and potential applications1. Most of these applications are based on their excellent piezoelectric properties or on their charge storage capability, exploited in non-volatile memory applications2,3. Nowadays, flurry of research is focused on ferroelectric tunnel junctions for novel memory applications4,5,6,7,8,9 and on photo-effects in ferroelectrics for their integration in solar cells10,11,12,13. In both applications, the role of internal electric fields is very important. In the former, internal fields determine the memory retention14 and in the latter internal electric fields determine the magnitude and direction of the photocurrents15,16,17,18,19,20,21. Two types of internal electric fields can be identified: the depolarizing field (Edep) and the imprint field (Eimp). The former (Edep) is opposite to the direction of the polarization, is responsible of the film depolarization and instigates breaking a single ferroelectric domain into a multi-domain structure. The latter (Eimp) drives ferroelectric polarization towards a preferential direction when biasing electric fields are removed.

Imprint fields can have different origins, such as asymmetric metal-dielectric interfaces, which may give rise to unequal Schottky barriers, or graded defect concentration22,23. Consequently, to reduce Eimp, electrode-ferroelectric-electrode structures should be made as symmetric as possible24. When dealing with ferroelectric thin films, a common approach is the use of a symmetric contact configuration in which the ferroelectric film is grown on a bottom metallic electrode and two identical top electrode pads are contacted. In this so-called, top-top measurement configuration, the two pads and the ferroelectric layer form a two capacitors series circuit connected via a common bottom electrode. As a result, symmetric polarization-vs-electric field loops can be obtained21,25. When applying an electric field (E) to the sample using the top-top configuration, the polarization P under each electrode points towards opposite directions. If an Eimp exists across the ferroelectric layer, under one electrode P is parallel to Eimp whereas under the other P is antiparallel to Eimp. Similarly, Eimp is parallel to the applied electric field E in one capacitor but antiparallel in the other. As the switching of every ferroelectric capacitor is dictated by the actual field acting on it, their switching should occur at different E values and thus fingerprints of Eimp on P-E loops must be observable. However, as mentioned, data collected using top-top configuration typically display symmetric P-E loops, suggesting a virtual cancellation of Eimp. To decipher the ultimate reasons for the absence of imprint signatures in these devices is crucial for their performance optimization and understanding.

In the present work, we study in detail the role of the Eimp on the switching process in devices formed by ferroelectric films [BaTiO3 (150 nm), BTO] grown on a metallic bottom electrode [La2/3Sr1/3MnO3 (50 nm), LSMO] using SrTiO3 (STO) substrates. Measurements are performed using an asymmetric contact configuration (bottom-top, sketched in Fig. 1a) and compared to those obtained in symmetric contact configuration constituted by two identical top metallic electrodes (top-top, Fig. 1b). It is found that when using top-top, no signatures of Eimp in current-field J-E and polarization-field P-E loops are observed if measurements are performed at relatively low frequencies, thus indicating the Eimp does not show up. However, when loops are recorded at higher frequency, a two-step ferroelectric switching becomes visible, which signals the presence of Eimp. We argue that these results indicate that the absence of Eimp fingerprints in P(E) loops recorded using in symmetric top-top configuration, is the result of a dynamic charge polarization screening process rather than an equilibrium property of the device. Consistently, we show that single or two-step P-E loops can be obtained in a given device at a given frequency, by on-purpose modification of the screening of the polarization by using photogenerated carriers. We claim that the commonly observed symmetric P-E loops in top-top symmetric electrode configuration is the result of a simultaneous switching of the polarization of the ferroelectric layers of each capacitor to avoid unfavourable head-to-head/tail-to-tail domain configuration, while the Eimp is still present. These conclusions, which have been verified by experiments performed on a variety of BaTiO3 films grown on different substrates and using different bottom electrodes and also on BaTiO3 single crystals, should help to the better understanding of the response of ferroelectric-based memories and of photo-effects arising in ferroelectric materials.

Figure 1

(a) Sketch of bottom-top (b-t) electrodes configuration for BTO (150 nm)/LSMO (50 nm)//STO sample. Top electrodes (yellow) represent the Pt top electrodes. (b) Sketch of top-top (t-t) electrodes configuration. (c,e,g) J-E loops measured in b-t at 15, 50 and 200 Hz, respectively. (d,f,h) J-E loops measured in t-t at 15, 50 and 200 Hz, respectively. The coercive field of single-switching-peak loops (Ec) and the corresponding Ec1, Ec2 of double-switching-peaks loops are indicated by the (red) dashed lines. Coercive fields are only depicted for the branches of increasing applied E-field.



BaTiO3 (150 nm)/La2/3Sr1/3MnO3(50 nm) bilayers were grown by pulsed laser deposition on (001) SrTiO3 substrates. 20 nm thick Pt top electrodes with dimension of 60 × 60 μm2 and 15 μm apart (see Methods), were deposited ex-situ on the BTO surface by RF-sputtering. For comparison purposes, BaTiO3 thin films on other substrates [DyScO3 (DSO) and (La,Sr)(Al,Ta)O3 (LSAT)], or using other metallic bottom electrodes [SrRuO3 (SRO)] have also been tested, Consistent results have been obtained in all cases. We have also measured a BaTiO3 single crystal (1 mm thick). In bottom-top (b-t) configuration (Fig. 1a), the bias voltage (V) was applied to one of the top electrodes and the bottom electrode was grounded. In top-top (t-t) configuration (Fig. 1b), one top electrode was biased and the other was grounded. Ferroelectricity was characterized by measuring the dynamic I-V hysteresis loop to determine the switchable polarization P (see Methods).

Polarization switching in symmetric and asymmetric double capacitors

Figure 1c–h show the J-E loops (arrows indicate the sense of the electric field excursion) recorded at various frequencies using b-t and t-t configurations, respectively. The corresponding P-E loops are shown in Supplementary Note 1 and Supplementary Fig. S1. In b-t configuration (Fig. 1c,e,g), it can be observed that, irrespective of the measurement frequency, the current switching peaks (indicated by dashed lines for increasing voltage) occurring at the coercive field (Ec), are shifted along the positive electric field axis. This is a signature of the presence of Eimp that, in the present case, is pointing away from LSMO. A similar imprint direction has been determined by other authors on similar heterostructures26. From loops measured at 15 Hz we derive: Eimp = (Ec+ + Ec−)/2 is 121.5 kV cm−1 and a coercive field Ec = (Ec+ − Ec−)/2 of about 100 kV cm−1. E are the coercive fields measured at positive and negative fields, respectively. As mentioned, it is known that Eimp can originate from a variety of effects, the most obvious one being a difference of work functions of the used electrodes; in the b-t configuration: LSMO and Pt, respectively. Although other mechanisms could play a role, the important point here is that Eimp is well visible and points away from LSMO. Tests performed on other b-t contacts yield similar Eimp values. The same orientation of Eimp had also been found in similar LSMO/BTO/Pt heterostructures and it was shown to be compatible with the different of screening ability of LSMO and Pt electrodes27.

The results obtained using t-t contacts are radically different. Indeed, in Fig. 1d it can be appreciated that in the J-E loop measured at 15 Hz, the current switching peaks appear at symmetric electric field values thus indicating that Eimp has seemingly disappeared. This observation implies that the polarization directions of the two in-series ferroelectric capacitors have switched at the same electric field. The coercive field Ec (≈100 kV cm−1) is identical to that determined in the b-t configuration.

A hint to identify the underlying mechanism for the absence of Eimp in the low-frequency can be obtained by inspecting the corresponding J-E loops recorded at higher frequencies (Fig. 1f,h). At 50 Hz (Fig. 1f) the ferroelectric switching current peak becomes broader and a tiny additional current peak appears (both signalled by dashed lines for increasing electric field). At even higher frequency (200 Hz) the presence of two switching peaks and their splitting are more evident (Fig. 1h). This implies that the polarization switching in the two in-series capacitor device occurs as a two-step process, controlled by two different coercive fields. In brief, two switching peaks in Fig. 1f,h appear at different E-fields and their separation increases when increasing the measuring frequency. The fact that a double-switching current peak is clearly observable in the t-t but not in b-t measurements, indicates that it results from the measurement configuration rather than from an intrinsic property of the ferroelectric layer.

Similar experiments have been performed on other BaTiO3 thin films grown on different substrates [SrTiO3, DyScO3 and (La,Sr)(Al,Ta)O3] and/or using different bottom electrodes (La2/3Sr1/3MnO3 and SrRuO3). A BaTiO3 single crystal where different electrodes have been deposited on opposite, faces has also been tested. In all cases, consistent results have been obtained (see results of BTO/LSMO//DSO and single crystal BTO in Supplementary Note 2 and Supplementary Figs S2 and S3).

Summarizing, when using t-t configuration, the J-E loops recorded at low frequency display a single-switching current peak whereas at high frequency, two switching peaks splits are visible. In order to understand these results we sketch in Fig. 2a–c the expected voltage-dependent polarization of two ferroelectric capacitors connected in series through a common LSMO bottom electrode. In agreement with b-t experiments (Fig. 1c,e,g), the imprint field Eimp is depicted (small empty arrow) pointing away from LSMO. We sketch the ferroelectric polarization (P) direction (large solid arrow) for the two ferroelectric capacitors for different values of decreasing applied electric field (from V+ to V). In Fig. 2a, we show the situation occurring when an electric field (V+ > 0) large enough (E+Ec, Eimp) to saturate the ferroelectric with the polarization pointing towards the ground, defined as negative (pointing towards the left in the figure), is applied. The polarization in both capacitors will point to the direction imposed by E+; note that the electric imprint is parallel to the polarization in one capacitor (left), but antiparallel in the other (right). When the electric field intensity reverses polarity (E), at some E = Ec1− = Ec − Eimp, the polarization in the right capacitor will switch; notice that│Ec1│ < │Ec│ because Eimp adds to help in the switching of the polarization (Fig. 2b). When the electric field is further increased (in modulus), at Ec2− = Ec + Eimp (Fig. 2c) the polarization in the left capacitor would switch as well; notice that│Ec2│ > │Ec│ because now Eimp is opposite to the applied electric field and thus a larger E-field is required to induce its switching. As a consequence, if imprint were to act, a “two-step” switching would occur and it will produce distinctive features at Ec − Eimp and Ec + Eimp in the J-E hysteresis loop. Thus as sketched in Fig. 2d, the J-E hysteresis loop should display two ferroelectric switching peaks. In the experimental loops of Fig. 1(f,h), these double peaks are well visible. They are superimposed to the displacive current (id) resulting from the fact that the capacitors are charging/discharging upon voltage cycling (id = −dQ/dt = −dQ/dV·dV/dt = −C·dV/dt).

Figure 2

Sketches of the polarization state of the series connection of the ferroelectric capacitors of the t-t configuration, during switching in presence of Eimp.

Solid (green) arrows indicate the direction of P and empty (red) arrows the direction of Eimp. (a) Electric field smaller than Ec − Eimp: P in both capacitors point towards the same direction, negative. (b) Electric field slightly larger than Ec − Eimp: P in the right capacitor switches resulting in a “tail-to-tail” domain configuration. (c) Electric field slightly larger than Ec + Eimp: the domains in the left capacitor flip, P in both capacitors point towards the same direction positive. (d) Schematic diagram of the corresponding J-E loop recorded while applying a triangular voltage pulse to the device. The pair of switching-peaks and the position of two coercive fields Ec1, Ec2 on the return (V+ to V) part of the loop are marked by dashed lines.

It can be observed in Fig. 1h that Ec1+ = −25 kV cm−1 and Ec2+ = +200 kV cm−1 at 200 Hz. These “effective” coercive field values are in good agreement with those that can be derived from the experimental Ec and Eimp determined from J-E loops recorded in b-t configuration (Fig. 1c,e,g): Ec1 = Ec − Eimp = −21.5 kV cm−1 and Ec2 = Ec + Eimp = +221.5 kV cm−1, confirming that the scenario depicted in Fig. 2a,b collects the physics behind. A similar analysis has been performed in other samples and coherent with results obtained. In Table 1 we collect: the Eimp and Ec values extracted from b-t and t-t configurations, respectively, at low frequency regime; the estimated values of Ec1 and Ec2; and experimental values of Ec1 and Ec2 at high frequency regime (see corresponding J-E loops in Supplementary Fig. S4). It can be observed that estimated and experimental values of Ec1 and Ec2 are in good agreement in samples grown on LSAT and STO irrespectively on the bottom electrode (LSMO or SRO) used. Similar good agreement is obtained for BTO/SRO//DSO sample. It is remarkable that irrespective from their slightly different structural properties (Supplementary Note 3 and Supplementary Fig. S5), the estimated and measured Ec1 and Ec2 values for all samples nicely agree. However, for the BTO/LSMO//DSO sample, the Ec value extracted from b-t and t-t configurations are unexpectedly different (161 and 225 kV cm−1, respectively). We assign this discrepancy to the fact that the properties of the bottom LSMO layer in this particular sample may be different as its anomalously shorter out-of-plane cell parameter anticipates (see Supplementary Fig. S5).

Table 1 Experimental and estimated values of Ec1, Ec2 of five different BTO thin film samples, grown on different substrates and using different bottom electrodes.

The two-step switching is signalled by the corresponding double current peaks observed in the high frequency t-t measurements; it reveals that even in the t-t configuration the Eimp is acting. However, it is not apparent in the low frequency J-E measurements. To rationalize this observation, it is worth to notice that if two-step switching process would occur, the ferroelectric capacitors would be connected head-to-head and tail-to-tail through the common bottom electrode (LSMO) as shown in Fig. 2b, which is floating, i.e. it is not grounded nor connected to a charge reservoir. This entails a poor polarization screening efficiency by the bottom electrode. Consequently, head-to-head/tail-to-tail configuration is energetically unfavourable and should revert to the stable head-to-tail/tail-to-head configurations. That is plausibly the reason why one can only indirectly observe the presence of this unfavourable domain configuration at high measurement frequencies. Switching from head-to-head (tail-to-tail) to tail-to-head (head-to-tail) occurs in the time scale of the measurement because a single current switching peak observed at low frequency. This indicates that the characteristic time for charge redistribution to screen unfavourably oriented domains is of about τ = 0.5/f ≈ 30 ms.

The J-E response in ferroelectric capacitors is dictated by the ability of the system to efficiently screen the polarization charges and illumination of semiconducting electrodes had been used to tailor screening and the amount of switchable polarization in ferroelectric thin films28. Similarly, in the experiments described above, one can envisage to modulate the polarization screening by inducing photoelectrons by photon absorption at the ferroelectric layer, which in turn will modify the required screening charge density at electrodes and subsequently the relative stability of tail-to-tail and tail-to-head polarization configurations.

Photoresponsive double capacitors

Aiming to test this proposal, we have illuminated the sample by using blue photons (3.06 eV), which it is known that can be absorbed by BaTiO3 thin films29 and we have recorded the J-E loops in t-t configuration at the same frequencies than in Fig. 1. The results are presented in Fig. 3a–c. In Fig. 3a, we show the data collected at 15 Hz. It can be observed that the magnitude of the switching current peaks measured under illumination is definitely smaller than that recorded in dark (Fig. 1). This is because photocarriers contribute to screen the polarization upon P reversal thus modifying the displacive current flowing in the external measuring circuit20. This is confirmed by the absence of any significant effect when similar experiments are performed using light of longer wavelength (see Supplementary Note 4 and Supplementary Fig. S6). Of higher relevance for the present work is the fact that in these low frequency measurements (Fig. 3a), one can observe the emergence of two current switching peaks, which were not present in the measurements performed without illumination (Fig. 1d). These two current switching peaks evolve when increasing the measuring frequency and become fully visible at 50 Hz and 200 Hz (Fig. 3b,c, respectively) whereas they were only incipient under dark conditions (Fig. 1f). These measurements indicate that under illumination, polarization switching of the two in-series ferroelectric capacitors does not proceed as a single event (within the experimental time window) but as a double-step and thus it mimics the high frequency dark response (Fig. 1d,f,h). This result is in full agreement with the picture of photocarriers modifying the electrostatic boundary conditions, namely the polarization screening, in such a way that tail-to-tail and head-to-head polar states become more stable.

Figure 3

The J-E loops of sample BTO/LSMO//STO measured by t-t under illumination, at 15 Hz (a), 50 Hz (b), 200 Hz (c), respectively. The coercive fields Ec1+, Ec2+ recorded on the increasing branch of the J-E are indicated (dashed lines).

J-E curves, similar to those show in Figs 1d,f,h and 3a–c, recorded in dark and under illumination respectively, have been measured in a range of frequencies and used to determine the frequency dependence of the coercive fields in the ascending (Ec1+ and Ec2+) and decreasing (Ec1− and Ec2−) branches of the voltage excursion. Data are summarized in Fig. 4, where the frequency dependence of Ec1± and Ec2± is plotted. It can be appreciated that irrespectively if the sample is in dark (Fig. 4a) or under illumination (Fig. 4b), the splitting between Ec1+ and Ec2+ (and between Ec1− and Ec2−) gradually increases when increasing frequency, indicating that faster measuring allows getting access to the unstable head-to-head and tail-to-tail configurations, having distinguishable impact on the shape of the recorded J-E. The frequency at which the two-step switching starts to be visible should be in principle limited by the electronic reordering at top or bottom electrodes, which are primarily responsible for charge screening. However, it can be appreciated in Fig. 4 that at a frequency as low as about 15 Hz, the two peaks begin to be visible. This leads to a response time τ ≈ 30 ms; this slow reaction time is at odds with the view that electronic transport within the electrodes determines the response time. Moreover, it is experimentally observed that the frequency dependence of the J(E) curves is independent on the distance between the t-t electrodes (either neighboring or further apart) (Supplementary Note 5 and Supplementary Fig. S7). These observations confirm that the bulk properties of the LSMO bottom electrode do not play a role. On the other hand, as the majority carrier mobility in BaTiO3 (typically BTO is a n-type semiconductor) is of about 1 cm2 V−1 s−1 and the depolarizing filed is of about 10 kV cm−1, the transit time for a layer of about 100 nm is expected to be much shorter (<1 ns) than the time scale (τ) of relevance in the present experiments. Therefore, neither carriers in the electrodes nor the majority carriers in the ferroelectric seems to determine τ. This conclusion is further supported by the observation that the resistance of the device decreases upon illumination (blue laser) and rapidly recovers when illumination is switched off. In contrast, although the capacitance of the device is reduced under illumination, it does not revers back to the initial state (Supplementary Note 6 and Supplementary Fig. S8), thus indicating that the change of impedance of the system is due to reordering of slow-moving charges rather than majority carriers. Therefore, minority carrier diffusion and/or ionic transport in BaTiO3, which are both slower processes30, appear to govern the observed transient response. We strength that the time constant of our measuring circuit is also much shorter (≈240 μs, see Supplementary Note 7 and Supplementary Fig. S9) and thus it cannot be relevant in the observed time response. Thus, data suggest that charge screening and concomitantly the head-to-head/tail-to-tail life-time, might be, at least partially, satisfied by electronic charge (holes) and ions in n-type BaTiO3.

Figure 4

Dependence of the coercive fields on frequency, in dark (a) and under illumination (b). (Ec1+, Ec2+) and (Ec1−, Ec2−) indicate the position of the switching current peaks observed in the ascending and decreasing branches of the J-E loops, respectively.


Polarization of ferroelectric thin films is often explored using contact pads placed at the film’s surface and a common metallic layer underneath is used as bottom electrode (top-top configuration). In this arrangement, the device under test is equivalent to two in-series ferroelectric capacitors connected via the common bottom electrode. Identical contacts may, in-principle, avoid asymmetric interface-related build-in electric fields, thus minimizing electric imprint Eimp fields. Here, we have shown that in presence of Eimp, in t-t configuration, J-E loops without any signature of Eimp are only obtained when measurements are performed at relatively low frequency, whereas distinctive double-step appear when J-E is recorded at high frequency. We have shown here these effects result from the non-cancellation of imprint field, which however, only shows up at higher frequency. We have argued that the observation of double-step in J-E is a consequence of the short-living head-to-head and tail-to-tail ferroelectric domains. In other words, Eimp may not be apparent in J-E and P-E loops, but it is not cancelled in symmetric t-t configuration. We have also demonstrated that modifying the charge screening capability of the device by suitable photogenerated carrier injection, allows modulating the relative stability of head-to-head (tail-to-tail) respect to tail-to-head (head-to-tail) ferroelectric domain configuration. Finally, we have proposed that in symmetric top-top electrode measuring configuration, polarization screening is partially provided by internal charges in BaTiO3 which permit the camouflage of imprint fields without cancelling it. These findings may be of particular relevance in the field of photoresponse of ferroelectric films, where polarization screening plays a fundamental role.


BaTiO3(150 nm)/La2/3Sr1/3MnO3(50 nm) bilayers were grown in a single process by pulsed laser deposition on (001) SrTiO3 substrates using a quadrupled Q-Switched Nd:YAG laser (λ = 266 nm) with a fluence of 5.2 J cm−2 for LSMO deposition process. For BTO growth, we used a fluence of 2.2 J cm−2 and a repetition rate of 2 Hz. LSMO films were grown at a deposition temperature of 730 °C and an oxygen pressure of 0.22 Torr. The growth of BTO was performed at 640 °C, with an oxygen pressure of 0.02 Torr and it was followed by an annealing at 600 °C in a high oxygen pressure (760 Torr) during 30 min. After cooling down to room temperature, 20 nm thick Pt top electrodes were deposited on BTO surface by RF-sputtering ex-situ, by using a 300 mesh mask allowing to deposit about 600 electrodes (60 × 60 μm2, 15 μm distance apart). X-ray reciprocal space maps showed that the LSMO layer is epitaxial and fully strained whereas the pattern of BTO layer manifests an elongated out-of-plane parameter and a near relaxed in-plane cell parameter (Supplementary Note 8 and Supplementary Fig. S10). For comparison purposes, BaTiO3 thin films on other substrates [DyScO3 and (La,Sr)(Al,Ta)O3], using other metallic bottom electrodes (SrRuO3) and a BaTiO3 single crystal have also been tested giving consistent results.

In b-t configuration (Fig. 1a), the bias voltage (V) was applied to one top electrode and the bottom electrode was grounded. In t-t configuration (Fig. 1b), one top electrode was biased and the other was grounded. Unless explicitly indicated, the two electrodes used in t-t are always adjacent. Ferroelectricity was characterized by applying triangular V-t pulses of frequencies ranging from 15 Hz to 2 kHz and measuring the dynamic I-V hysteresis loops, using a TFAnalyzer2000 (aixACCT Systems GmbH) to determine the switchable polarization P. The current density (J) is evaluated as J = I/A where A is the electrode area. The electric field is evaluated as E = V/δ or V/(2δ) for the b-t and t-t configurations respectively (δ is the ferroelectric film thickness). Further details on measurement protocols can be found elsewhere31.

Loops measured under illumination were collected by lighting up the electrodes with a laser of wavelength 405 nm fed by a CPX400SA DC power source (AimTTi Co.). Loops are recorded after sufficient illumination time to saturate the effect. The used photons (3.06 eV) are of sub-bandgap energy (3.3 eV for BTO29). It is known that oxygen deficiencies (or other point defects) in BaTiO3 can introduce donor states which give rise to a photoresponse under sub-bandgap illumination32,33,34. The spot diameter is of 200 μm, which largely covers two electrodes, allowing a homogeneous illumination with a power of 3 W cm−2.

Additional Information

How to cite this article: Liu, F. et al. Unravelling and controlling hidden imprint fields in ferroelectric capacitors. Sci. Rep. 6, 25028; doi: 10.1038/srep25028 (2016).


  1. Scott, J. F. Applications of modern ferroelectrics. Science 315, 954–959 (2007).

    CAS  ADS  Article  Google Scholar 

  2. Scott, J. F. & Paz de Araujo, C. A. Ferroelectric memories. Science 246, 1400–1405 (1989).

    CAS  ADS  Article  Google Scholar 

  3. Trolier-Mckinstry, S. & Muralt, P. Thin film piezoelectrics for MEMS. J. Electroceram. 12, 7–17 (2004).

    CAS  Article  Google Scholar 

  4. Tsymbal, E. Y. & Kohlstedt, H. Tunneling across a ferroelectric. Science 313, 181–183 (2006).

    CAS  Article  Google Scholar 

  5. Maksymovych, P. et al. Polarization control of electron tunneling into ferroelectric surfaces. Science 324, 1421–1425 (2009).

    CAS  ADS  Article  Google Scholar 

  6. Garcia, V. et al. Giant tunnel electroresistance for non-destructive readout of ferroelectric states. Nature 460, 81–84 (2009).

    CAS  ADS  Article  Google Scholar 

  7. Chanthbouala, A. et al. Solid-state memories based on ferroelectric tunnel junctions. Nat. Nanotechnol. 7, 101–104 (2012).

    CAS  ADS  Article  Google Scholar 

  8. Garcia, V. & Bibes, M. Ferroelectric tunnel junctions for information storage and processing. Nat. Commun. 5, 4289 (2014).

    CAS  ADS  Article  Google Scholar 

  9. Barrionuevo, D. et al. Tunneling electroresistance in multiferroic heterostructures. Nanotechnology 25, 495203 (2014).

    CAS  Article  Google Scholar 

  10. Yang, S. Y. et al. Above-bandgap voltages from ferroelectric photovoltaic devices. Nat. Nanotechnol. 5, 143–147 (2010).

    CAS  ADS  Article  Google Scholar 

  11. Kundys, B., Viret, M., Colson, D. & Kundys, D. O. Light-induced size changes in BiFeO3 crystals. Nat. Mater. 9, 803–805 (2010).

    CAS  ADS  Article  Google Scholar 

  12. Alexe, M. & Hesse, D. Tip-enhanced photovoltaic effects in bismuth ferrite. Nat. Commun. 2, 256 (2011).

    ADS  Article  Google Scholar 

  13. Bhatnagar, A., Chaudhuri, A. R., Kim, Y. H., Hesse, D. & Alexe, M. Role of domain walls in the abnormal photovoltaic effect in BiFeO3 . Nat. Commun. 4, 2835 (2013).

    ADS  Article  Google Scholar 

  14. Tagantsev, A. K. & Gerra, G. Interface-induced phenomena in polarization response of ferroelectric thin films. J. Appl. Phys. 100, 051607 (2006).

    ADS  Article  Google Scholar 

  15. Brody, P. S. & Rod, B. J. Decay of remanent polarization in ferroelectric films using polarization-dependent photovoltages. Integr. Ferroelectr. 3, 245–257 (1993).

    CAS  Article  Google Scholar 

  16. Ji, W., Yao, K. & Liang, Y. C. Bulk photovoltaic effect at visible wavelength in epitaxial ferroelectric BiFeO3 thin films. Adv. Mater. 22, 1763–1766 (2010).

    CAS  Article  Google Scholar 

  17. Pintilie, L., Stancu, V., Vasile, E. & Pintilie, I. About the complex relation between short-circuit photocurrent, imprint and polarization in ferroelectric thin films. J. Appl. Phys. 107, 114111 (2010).

    ADS  Article  Google Scholar 

  18. Zhang, J. et al. Enlarging photovoltaic effect: combination of classic photoelectric and ferroelectric photovoltaic effects. Sci. Rep. 3, 2109 (2013).

    Article  Google Scholar 

  19. Yang, Y. S. et al. Schottky barrier effects in the photocurrent of sol-gel derived lead zirconate titanate thin film capacitors. Appl. Phys. Lett. 76, 774–776 (2000).

    CAS  ADS  Article  Google Scholar 

  20. Qin, M., Yao, K. & Liang, Y. C. Photovoltaic mechanisms in ferroelectric thin films with the effects of the electrodes and interfaces. Appl. Phys. Lett. 95, 022912 (2009).

    ADS  Article  Google Scholar 

  21. Liu, F. et al. Selecting steady and transient photocurrent response in BaTiO3 thin films. Adv. Electron. Mater. 1, 1500171 (2015).

    Article  Google Scholar 

  22. Zhou, Y., Chan, H. K., Lam, C. H. & Shin, F. G. Mechanisms of imprint effect on ferroelectric thin films. J. Appl. Phys. 98, 024111 (2005).

    ADS  Article  Google Scholar 

  23. Koval, V., Viola, G. & Tan, Y. In Ferroelectric Materials-Synthesis and Characterization (ed. Barranco, A. P. ) Ch. 9, (InTech, Croatia, 2015).

  24. Rault, J. E. et al. Interface electronic structure in a metal/ferroelectric heterostructure under applied bias. Phys. Rev. B 87, 155146 (2013).

    ADS  Article  Google Scholar 

  25. Evans, Jr., J. T. & Cardoza, H. E. The imprint mechanism in ferroelectric capacitors. Integr. Ferroelectr. 10, 267–277 (1995).

    Article  Google Scholar 

  26. Cui, B. et al. Magnetoelectric coupling induced by interfacial orbital reconstruction. Adv. Mater. 27, 6651–6656 (2015).

    CAS  Article  Google Scholar 

  27. Radaelli, G. et al. Large room-temperature electroresistance in dual-modulated ferroelectric tunnel barriers. Adv. Mater. 27, 2602–2607 (2015).

    CAS  Article  Google Scholar 

  28. Wurfel, P. & Batra, I. P. Depolarization-field-induced instability in thin ferroelectric films—experiment and theory. Phys. Rev. B 8, 5126–5133 (1973).

    CAS  ADS  Article  Google Scholar 

  29. Wemple, S. H. Polarization fluctuations and the optical-absorption edge in BaTiO3 . Phys. Rev. B 2, 2679–2689 (1970).

    ADS  Article  Google Scholar 

  30. Wang, J. L., Vilquin, B. & Barrett, N. Screening of ferroelectric domains on BaTiO3(001) surface by ultraviolet photo-induced charge and dissociative water adsorption. Appl. Phys. Lett. 101, 092902 (2012).

    ADS  Article  Google Scholar 

  31. Fina, I. et al. Nonferroelectric contributions to the hysteresis cycles in manganite thin films: A comparative study of measurement techniques. J. Appl. Phys. 109, 074105 (2011).

    ADS  Article  Google Scholar 

  32. Moreira, M. L. et al. Photoluminescence of barium titanate and barium zirconate in multilayer disordered thin films at room temperature. J. Phys. Chem. A 112, 8938–8942 (2008).

    CAS  Article  Google Scholar 

  33. Chang, J. Y., Garrett, M. H., Jenssen, H. P. & Warde, C. Intensity dependent absorption/ transparency of a reducing BaTiO3 . Appl. Phys. Lett. 63, 3598–3600 (1993).

    CAS  ADS  Article  Google Scholar 

  34. Zhao, T. et al. Electrical and optical properties of strongly reduced epitaxial BaTiO3−x thin films. Appl. Phys. Lett. 77, 4338–4340 (2000).

    CAS  ADS  Article  Google Scholar 

Download references


This work is supported by the Spanish Government (MAT2014-56063-C2-1-R) and by the Catalan Government (2014 SGR 734). ICMAB-CSIC authors acknowledge financial support from the Spanish Ministry of Economy and Competitiveness, through the “Severo Ochoa” Programme for Centres of Excellence in R&D (SEV- 2015-0496). Ignasi Fina acknowledges the Beatriu de Pinós postdoctoral scholarship (2011 BP-A_2 00014) from AGAUR-Generalitat de Catalunya. Fanmao Liu is financially supported by China Scholarship Council (CSC) with No. 201306020016. We are thankful to F. Sánchez and M. Cantoni, for growing the films and making the preliminary characterization of the films and to M. Stengel for inspiring discussions.

Author information




J.F., I.F. and F.L. jointly designed and conceived the experiments. The experimental set-up and experiments were built and conducted by F.L. I.F. and J.F. wrote the paper. All authors (F.L., I.F., R.B. and J.F.) discussed data and commented on the paper.

Ethics declarations

Competing interests

The authors declare no competing financial interests.

Electronic supplementary material

Rights and permissions

This 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

Reprints and Permissions

About this article

Verify currency and authenticity via CrossMark

Cite this article

Liu, F., Fina, I., Bertacco, R. et al. Unravelling and controlling hidden imprint fields in ferroelectric capacitors. Sci Rep 6, 25028 (2016).

Download citation

Further reading


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.


Quick links

Nature Briefing

Sign up for the Nature Briefing newsletter — what matters in science, free to your inbox daily.

Get the most important science stories of the day, free in your inbox. Sign up for Nature Briefing