There has been much recent interest in a so-called “giant-dielectric phenomenon” displayed by an unusual cubic perovskite-type material, CaCu3Ti4O12; however, the origin of the high permittivity has been unclear [M. A. Subramanian, L. Dong, N. Duan, B. A. Reisner, and A. W. Sleight, J. Solid State Chem. 151, 323 (2000); C. C. Homes, T. Vogt, S. M. Shapiro, S. Wakimoto, and A. P. Ramirez, Science 293, 673 (2001); A. P. Ramirez, M. A. Subramanian, M. Gardel, G. Blumberg, D. Li, T. Vogt, and S. M. Shapiro, Solid State Commun. 115, 217 (2000)]. Impedance spectroscopy on CaCu3Ti4O12 ceramics demonstrates that they are electrically heterogeneous and consist of semiconducting grains with insulating grain boundaries. The giant-dielectric phenomenon is therefore attributed to a grain boundary (internal) barrier layer capacitance (IBLC) instead of an intrinsic property associated with the crystal structure. This barrier layer electrical microstructure with effective permittivity values in excess of 10 000 can be fabricated by single-step processing in air at ∼1100 °C. CaCu3Ti4O12 is an attractive option to the currently used BaTiO3-based materials which require complex, multistage processing routes to produce IBLCs of similar capacity.

Wang et al . ([ 1 ][1]) recently reported multiferroic behavior, with ferromagnetic and ferroelectric polarizations that are both large at room temperature, in thin strained films of BiFeO3 (BFO). Although at room temperature, bulk BFO is ferroelectric ([ 2 ][2]) and anti-ferromagnetic ([ 3 ][3]–[ 5 ][4]), Wang et al. ([ 1 ][1]) reported that a 70-nm film shows both an enhanced ferroelectric polarization (90 μC cm–2) and a substantial magnetization (1 μB/Fe). This remains the only report of a robust room-temperature multiferroic and suggests the potential for novel devices that exploit the anticipated strain-mediated magnetoelectric coupling between the two ordered ground states. In this Comment, we argue that epitaxial strain does not enhance the magnetization and polarization in BiFeO3. Like Wang et al. ([ 1 ][1]), we grew BFO films on 50-nm underlayers of SrRuO3 (SRO) on SrTiO3 (001) substrates (STO). In addition, we used plain STO and conducting 0.2% atomic Nb-doped SrTiO3 substrates (Nb-STO). Both BFO and SRO films were grown by pulsed laser deposition with a KrF excimer laser (248 nm, 1 Hz, target-substrate distance = 8cm). BFO films were grown (670°C, 8 Pa O2, 1.6 J cm–2) using a Bi-rich target of Bi1.2FeO3, because Bi is volatile ([ 6 ][5]). SRO films were grown (650°C, 9 Pa O2, 1.7 J cm–2) using a stoichiometric target. The growth rate for both BFO and SRO was 10 Å/min. After deposition, films were cooled at 5°C/min to 400°C in 40 kPa oxygen, annealed for 1 hour, and then cooled to room temperature at 8°C/min. The crystalline quality of our films was investigated with high-resolution x-ray diffraction ([Fig. 1][6]). The reciprocal space maps show that the BFO and SRO in-plane lattice parameters are equal to the STO lattice parameter of 3.905 Å, consistent with coherently strained films. It should be noted that Wang et al . ([ 1 ][1]) performed their calculations of saturation polarization using the bulk SRO lattice parameter of 3.935 Å for the BFO inplane lattice parameter. In our work, BFO films as thin as 40 nm gave equivalent x-ray results, but 300-nm BFO films were found to be relaxed. All coherently strained films showed a root-mean-square surface roughness of 2 nm, as determined by atomic force microscopy. ![ Fig. 1. ][7] Fig. 1. Ω-2θ scan of the (001) pseudocubic reflection for ( A ) BFO(80 nm)/Nb-STO and ( B ) BFO(90 nm)/SRO(50 nm)/STO. The corresponding reciprocal space maps of the (013) pseudocubic reflections are shown in ( C ) and ( D ). Reciprocal lattice units (rlu) Q x and Q y are equal to the inverse lattice spacing. All in-plane film lattice parameters can be seen to be equal to the STO lattice parameter of 3.905 Å. The BFO out-of-plane lattice parameter in both samples is 4.07 Å, and the corresponding value for SRO is 3.95 Å. BFO film stoichiometry was determined from quantitative energy dispersive x-ray spectroscopy in a thick (∼400 nm) film grown at a laser repetition rate of 2 Hz. The Fe:Bi ratio was found to be unity, within the error of the technique of a few percent. The Fe oxidation state was investigated for BFO/STO samples grown at 1 Hz and 2 Hz with x-ray photoelectron spectroscopy. All samples behaved similarly; a representative scan of the Fe 2p line is shown in [Fig. 2][8]. The position of this line is expected to be 711 eV for Fe3+ and 709.5 eV for Fe2+, and the position of the satellite is expected at 719 eV for Fe3+ and 716 eV for Fe2+ ([ 7 ][9]). From [Fig. 2][8], we deduce that the oxidation state of Fe in our BFO/STO films is Fe3+ and that there is no evidence for Fe2+ within a resolution of a few atomic percent. ![ Fig. 2. ][7] Fig. 2. X-ray photoelectron spectrum of the Fe 2p lines for BFO(40 nm)/STO. To verify that our BFO films are insulating and ferroelectric, we performed piezoresponse microscopy ([ 8 ][10]) on BFO/Nb-STO and BFO/SRO/STO, and impedance spectroscopy using sputter-deposited Pt on BFO/Nb-STO. The former technique confirmed ferroelectric switching. The latter technique showed our films to be low-loss (2% loss tangent in 10 kHz to 1 MHz) and nonconducting (resistivity >1010 Ωcm). The high-temperature conductivity data showed an activation energy of 1.03 ± 0.05 eV, compatible with only a small concentration of oxygen vacancies ([ 9 ][11], [ 10 ][12]). In agreement with the literature ([ 11 ][13]), the effective dielectric constant (10 kHz to 1 MHz) was found to be 70 ± 2 at ambient temperature, increasing to ∼375 at 550 K. Magnetic measurements were taken at room temperature with a Princeton Measurements Corporation (Princeton, NJ) vibrating sample magnetometer. In [Fig. 3][14], we plot saturation magnetization M s as a function of BFO film thickness. BFO films both with and without the SRO underlayer behave similarly, which precludes any substantial magnetic contribution from SRO. All BFO films show an essentially thickness-independent M s that is less than 0.06 μB/Fe, which rules out the strain-enhanced magnetization inferred by Wang et al. ([ 1 ][1]). Indeed, strain should not modify anti-ferromagnetic exchange interactions between singly occupied Fe3+ 3d orbitals. We note that density functional calculations ([ 12 ][15]) of unstrained BFO suggest a local magnetization of around 0.05 μB/Fe, consistent with the findings presented here. ![ Fig. 3. ][7] Fig. 3. Saturation magnetization M s of BFO films versus film thickness. Black squares, BFO/STO; red circles, BFO/SRO(50 nm)/STO; blue triangle, BFO/Nb-STO. The inset shows a typical hysteresis loop. Magnetometer axis inplane and parallel to STO [100]. Before taking magnetic measurements, we used emery paper to grind away silver dag from the sides and undersides of the substrates to eliminate spurious magnetic signals that we attribute to material originating from the heater block. The small M s that we observed is reminiscent of bulk...

Single phase La-doped ${\mathrm{BaTiO}}_{\mathrm{3}}$ with the formula ${\mathrm{Ba}}_{\text{1−x}}{\mathrm{La}}_x{\mathrm{Ti}}_{\text{1−x/4}}{\mathrm{O}}_{\mathrm{3}}:$ $\text{0⩽x⩽0.20}$ was prepared by solid state reaction of oxide mixtures at $\text{1350\hspace{0.05em}°}\mathrm{C},$ 3 days, in ${\mathrm{O}}_{\mathrm{2}}.$ The tetragonal distortion in undoped ${\mathrm{BaTiO}}_{\mathrm{3}}$ decreased with x and samples were cubic for $\text{x⩾0.05.}$ Both the tetragonal/cubic and orthorhombic/tetragonal transition temperatures decreased with x, but at different rates, and appeared to coalesce at $\text{x∼0.08.}$ The value of the permittivity maximum at the tetragonal/cubic phase transition in ceramic samples increased from $\text{∼10\hspace{0.05em}000}$ for $\text{x=0}$ at $\text{130\hspace{0.05em}°}\mathrm{C}$ to $\text{∼25\hspace{0.05em}000}$ for $\text{x=0.06}$ at $\text{∼−9\hspace{0.05em}°}\mathrm{C}.$ At larger x, the permittivity maximum broadened, showed “relaxor”-type frequency dependent permittivity characteristics and continued to move to lower temperatures. Samples fired in ${\mathrm{O}}_{\mathrm{2}}$ were insulating and showed no signs of donor doping whereas air-fired samples were semiconducting, attributable to oxygen loss.

A detailed investigation using variable temperature powder neutron diffraction demonstrates that ${\mathrm{BiFeO}}_3$ undergoes a phase transition from the ferroelectric $\alpha$ phase (rhombohedral, $R3c$) to a paraelectric $\beta$ phase (orthorhombic, $Pbnm$) between $820°\mathrm{C}$ and $830°\mathrm{C}$. Coexistence of both phases over a finite temperature interval, together with abrupt changes in key structural parameters, confirms that the transition is first order. The $\beta$ phase corresponds to a ${\mathrm{GdFeO}}_3$-type perovskite structure.