大学物理实验报告 英文版.doc

《大学物理实验报告 英文版.doc》由会员分享，可在线阅读，更多相关《大学物理实验报告 英文版.doc（8页珍藏版）》请在三一办公上搜索。

1、大学物理实验报告Ferroelectric Control of Spin PolarizationABSTRACTA current drawback of spintronics is the large power that is usually required for magnetic writing, in contrast with nanoelectronics, which relies on “zero-current,” gate-controlled operations. Efforts have been made to control the spin-relax

2、ation rate, the Curie temperature, or the magnetic anisotropy with a gate voltage, but these effects are usually small and volatile. We used ferroelectric tunnel junctions with ferromagnetic electrodes to demonstrate local, large, and nonvolatile control of carrier spin polarization by electrically

3、switching ferroelectric polarization. Our results represent a giant type of interfacial magnetoelectric coupling and suggest a low-power approach for spin-based information control.Controlling the spin degree of freedom by purely electrical means is currently an important challenge in spintronics (1

4、,2). Approaches based on spin-transfer torque (3) have proven very successful in controlling the direction of magnetization in a ferromagnetic layer, but they require the injection of high current densities. An ideal solution would rely on the application of an electric field across an insulator, as

5、 in existing nanoelectronics. Early experiments have demonstrated the volatile modulation of spin-based properties with a gate voltage applied through a dielectric. Notable examples include the gate control of the spin-orbit interaction in III-V quantum wells (4), the Curie temperatureTC(5), or the

6、magnetic anisotropy (6) in magnetic semiconductors with carrier-mediated exchange interactions; for example, (Ga,Mn)As or (In,Mn)As. Electric fieldinduced modifications of magnetic anisotropy at room temperature have also been reported recently in ultrathin Fe-based layers (7,8).A nonvolatile extens

7、ion of this approach involves replacing the gate dielectric by a ferroelectric and taking advantage of the hysteretic response of its order parameter (polarization) with an electric field. When combined with (Ga,Mn)As channels, for instance, a remanent control ofTCover a few kelvin was achieved thro

8、ugh polarization-driven charge depletion/accumulation (9,10), and the magnetic anisotropy was modified by the coupling of piezoelectricity and magnetostriction (11,12). Indications of an electrical control of magnetization have also been provided in magnetoelectric heterostructures at room temperatu

9、re (1317).Recently, several theoretical studies have predicted that large variations of magnetic properties may occur at interfaces between ferroelectrics and high-TCferromagnets such as Fe (1820), Co2MnSi (21), or Fe3O4(22). Changing the direction of the ferroelectric polarization has been predicte

10、d to influence not only the interfacial anisotropy and magnetization, but also the spin polarization. Spin polarization i.e., the normalized difference in the density of states (DOS) of majority and minority spin carriers at the Fermi level (EF) is typically the key parameter controlling the respons

11、e of spintronics systems, epitomized by magnetic tunnel junctions in which the tunnel magnetoresistance (TMR) is related to the electrode spin polarization by the Jullire formula (23). These predictions suggest that the nonvolatile character of ferroelectrics at the heart of ferroelectric random acc

12、ess memory technology (24) may be exploited in spintronics devices such as magnetic random access memories or spin field-effect transistors (2). However, the nonvolatile electrical control of spin polarization has not yet been demonstrated.We address this issue experimentally by probing the spin pol

13、arization of electrons tunneling from an Fe electrode through ultrathin ferroelectric BaTiO3(BTO) tunnel barriers (Fig. 1A). The BTO polarization can be electrically switched to point toward or away from the Fe electrode. We used a half-metallic La0.67Sr0.33MnO3(LSMO) (25) bottom electrode as a spin

14、 detector in these artificial multiferroic tunnel junctions (26,27). Magnetotransport experiments provide evidence for a large and reversible dependence of theTMRon ferroelectric polarization direction.Fig. 1(A) Sketch of the nanojunction defined by electrically controlled nanoindentation. A thin re

15、sist is spin-coated on the BTO(1 nm)/LSMO(30 nm) bilayer. The nanoindentation is performed with a conductive-tip atomic force microscope, and the resulting nano-hole is filled by sputter-depositing Au/CoO/Co/Fe. (B) (Top) PFM phase image of a BTO(1 nm)/LSMO(30 nm) bilayer after poling the BTO along

16、1-by-4m stripes with either a negative or positive (tip-LSMO) voltage. (Bottom) CTAFM image of an unpoled area of a BTO(1 nm)/LSMO(30 nm) bilayer. , ohms. (C) X-ray absorption spectra collected at room temperature close to the Fe L3,2(top), Ba M5,4(middle), and Ti L3,2(bottom) edges on an AlOx(1.5 n

17、m)/Al(1.5 nm)/Fe(2 nm)/BTO(1 nm)/LSMO(30 nm)/NGO(001) heterostructure. (D) HRTEM and (E) HAADF images of the Fe/BTO interface in a Ta(5 nm)/Fe(18 nm)/BTO(50 nm)/LSMO(30 nm)/NGO(001) heterostructure. The white arrowheads in (D) indicate the lattice fringes of 011 planes in the iron layer. 110 and 001

18、 indicate pseudotetragonal crystallographic axes of the BTO perovskite.The tunnel junctions that we used in this study are based on BTO(1 nm)/LSMO(30 nm) bilayers grown epitaxially onto (001)-oriented NdGaO3(NGO) single-crystal substrates (28). The large (180) and stable piezoresponse force microsco

19、py (PFM) phase contrast (28) between negatively and positively poled areas (Fig. 1B, top) indicates that the ultrathin BTO films are ferroelectric at room temperature (29). The persistence of ferroelectricity for such ultrathin films of BTO arises from the large lattice mismatch with the NGO substra

20、te (3.2%), which is expected to dramatically enhance ferroelectric properties in this highly strained BTO (30). The local topographical and transport properties of the BTO(1 nm)/LSMO(30 nm) bilayers were characterized by conductive-tip atomic force microscopy (CTAFM) (28). The surface is very smooth

21、 with terraces separated by one-unit-cellhigh steps, visible in both the topography (29) and resistance mappings (Fig. 1B, bottom). No anomalies in the CTAFM data were observed over lateral distances on the micrometer scale.We defined tunnel junctions from these bilayers by a lithographic technique

22、based on CTAFM (28,31). Top electrical contacts of diameter 10 to 30 nm can be patterned by this nanofabrication process. The subsequent sputter deposition of a 5-nm-thick Fe layer, capped by a Au(100 nm)/CoO(3.5 nm)/Co(11.5 nm) stack to increase coercivity, defined a set of nanojunctions (Fig. 1A).

23、 The same Au/CoO/Co/Fe stack was deposited on another BTO(1 nm)/LSMO(30 nm) sample for magnetic measurements. Additionally, a Ta(5 nm)/Fe(18 nm)/BTO(50 nm)/LSMO(30 nm) sample and a AlOx(1.5 nm)/Al(1.5 nm)/Fe(2 nm)/BTO(1 nm)/LSMO(30 nm) sample were realized for structural and spectroscopic characteri

24、zations.We used both a conventional high-resolution transmission electron microscope (HRTEM) and the NION UltraSTEM 100 scanning transmission electron microscope (STEM) to investigate the Fe/BTO interface properties of the Ta/Fe/BTO/LSMO sample. The epitaxial growth of the BTO/LSMO bilayer on the NG

25、O substrate was confirmed by HRTEM and high-resolution STEM images. The low-resolution, high-angle annular dark field (HAADF) image of the entire heterostructure shows the sharpness of the LSMO/BTO interface over the studied area (Fig. 1E, top).Figure 1Dreveals a smooth interface between the BTO and

26、 the Fe layers. Whereas the BTO film is epitaxially grown on top of LSMO, the Fe layer consists of textured nanocrystallites. From the in-plane (a) and out-of-plane (c) lattice parameters in the tetragonal BTO layer, we infer thatc/a= 1.016 0.008, in good agreement with the value of 1.013 found with

27、 the use of x-ray diffraction (29). The interplanar distances for selected crystallites in the Fe layer i.e., 2.03 (Fig. 1D, white arrowheads) are consistent with the 011 planes of body-centered cubic (bcc) Fe.We investigated the BTO/Fe interface region more closely in the HAADF mode of the STEM (Fi

28、g. 1E, bottom). On the BTO side, the atomically resolved HAADF image allows the distinction of atomic columns where the perovskite A-site atoms (Ba) appear as brighter spots. Lattice fringes with the characteristic 100 interplanar distances of bcc Fe (2.86 ) can be distinguished on the opposite side

29、. Subtle structural, chemical, and/or electronic modifications may be expected to occur at the interfacial boundary between the BTO perovskite-type structure and the Fe layer. These effects may lead to interdiffusion of Fe, Ba, and O atoms over less than 1 nm, or the local modification of the Fe DOS

30、 close toEF, consistent with ab initio calculations of the BTO/Fe interface (1820).To characterize the oxidation state of Fe, we performed x-ray absorption spectroscopy (XAS) measurements on a AlOx(1.5 nm)/Al(1.5 nm)/Fe(2 nm)/BTO(1 nm)/LSMO(30 nm) sample (28). The probe depth was at least 7 nm, as i

31、ndicated by the finite XAS intensity at the La M4,5edge (28), so that the entire Fe thickness contributed substantially to the signal. As shown inFig. 1C(top), the spectrum at the Fe L2,3edge corresponds to that of metallic Fe (32). The XAS spectrum obtained at the Ba M4,5edge (Fig. 1C, middle) is s

32、imilar to that reported for Ba2+in (33). Despite the poor signal-to-noise ratio, the Ti L2,3edge spectrum (Fig. C, bottom) shows the typical signature expected for a valence close to 4+ (34). From the XAS, HRTEM, and STEM analyses, we conclude that the Fe/BTO interface is smooth with no detectable o

33、xidation of the Fe layer within a limit of less than 1 nm.After cooling in a magnetic field of 5 kOe aligned along the 110 easy axis of pseudocubic LSMO (which is parallel to the orthorhombic 100 axis of NGO), we characterized the transport properties of the junctions at low temperature (4.2 K).Figu

34、re 2A(middle) shows a typical resistanceversusmagnetic fieldR(H) cycle recorded at a bias voltage of 2 mV (positive bias corresponds to electrons tunneling from Fe to LSMO). The bottom panel ofFig. 2Ashows the magnetic hysteresis loopm(H) of a similar unpatterned sample measured with superconducting

35、 quantum interference device (SQUID) magnetometry. When we decreased the magnetic field from a large positive value, the resistance dropped in the 50 to 250 Oe range and then followed a plateau down to 800 Oe, after which it sharply returned to the high-resistance state. We observed a similar respon

36、se when cycling the field back to large positive values. A comparison with them(H) loop indicates that the switching fields inR(H) correspond to changes in the relative magnetic configuration of the LSMO and Fe electrodes from parallel (at high field) to antiparallel (at low field). The magnetically

37、 softer LSMO layer switched at lower fields (50 to 250 Oe) compared with the Fe layer, for which coupling to the exchange-biased Co/CoO induces larger and asymmetric coercive fields (800 Oe, 300 Oe). The observedR(H) corresponds to a negativeTMR= (RapRp)/Rapof 17% RpandRapare the resistance in the p

38、arallel (p) and antiparallel (ap) magnetic configurations, respectively; see the sketches inFig. 2A. Within the simple Jullire model ofTMR(23) and considering the large positive spin polarization of half-metallic LSMO (25), this negativeTMRcorresponds to a negative spin polarization for bcc Fe at th

39、e interface with BTO, in agreement with ab initio calculations (1820).Fig. 2(A) (Top) Device schematic with black arrows to indicate magnetizations. p, parallel; ap, antiparallel. (Middle)R(H) recorded at 2 mV and 4.2 K showing negativeTMR. (Bottom)m(H) recorded at 30 K with a SQUID magnetometer. em

40、u, electromagnetic units. (B) (Top) Device schematic with arrows to indicate ferroelectric polarization. (Bottom)I(VDC) curves recorded at 4.2 K after poling the ferroelectric down (orange curve) or up (brown curve). The bias dependence of theTERis shown in the inset.As predicted (3538) and demonstr

41、ated (29) previously, the tunnel current across a ferroelectric barrier depends on the direction of the ferroelectric polarization. We also observed this effect in our Fe/BTO/LSMO junctions. As can be seen inFig. 2B, after poling the BTO at 4.2 K to orient its polarization toward LSMO or Fe (with a

42、poling voltage ofVP 1 V orVP+ 1 V, respectively; seeFig. 2Bsketches), current-versus-voltageI(VDC) curves collected at low bias voltages showed a finite difference corresponding to a tunnel electroresistance as large asTER= (IVP+IVP)/IVP 37% (Fig. 2B, inset). ThisTERcan be interpreted within an elec

43、trostatic model (3639), taking into account the asymmetric deformation of the barrier potential profile that is created by the incomplete screening of polarization charges by different Thomas-Fermi screening lengths at Fe/BTO and LSMO/BTO interfaces. Piezoelectric-relatedTEReffects (35,38) can be ne

44、glected as the piezoelectric coefficient estimated from PFM experiments is too small in our clamped films (29).TERmeasurements performed on a BTO(1 nm)/LSMO(30 nm) bilayer with the use of a CTAFM boron-doped diamond tip as the top electrode showed values of 200% (29). Given the strong sensitivity of

45、 theTERon barrier parameters and barrier-electrode interfaces, these two values are not expected to match precisely. We anticipate that theTERvariation between Fe/BTO/LSMO junctions and CTAFM-based measurements is primarily the result of different electrostatic boundary conditions.Switching the ferr

46、oelectric polarization of a tunnel barrier with voltage pulses is also expected to affect the spin-dependent DOS of electrodes at a ferromagnet/ferroelectric interface. Interfacial modifications of the spin-dependent DOS of the half-metallic LSMO by the ferroelectric BTO are not likely, as no states

47、 are present for the minority spins up to 350 meV aboveEF(40,41). For 3d ferromagnets such as Fe, large modifications of the spin-dependent DOS are expected, as charge transfer between spin-polarized empty and filled states is possible. For the Fe/BTO interface, large changes have been predicted thr

48、ough ab initio calculations of 3d electronic states of bcc Fe at the interface with BTO by several groups (1820).To experimentally probe possible changes in the spin polarization of the Fe/BTO interface, we measuredR(H) at a fixed bias voltage of 50 mV after aligning the ferroelectric polarization o

49、f BTO toward Fe or LSMO.R(H) cycles were collected for each direction of the ferroelectric polarization for two typical tunnel junctions of the same sample (Fig. 3, B and C, for junction #1;Fig. 3, D and E, for junction #2). In both junctions at the saturating magnetic field, high- and low-resistance states are observed when the ferroelectric polarization points toward LSMO or Fe, respectively,