García-Barriocanal et al. (Reports, 1 August 2008, p. 676) reported colossal conductivity enhancements in yttria-stabilized zirconia (YSZ)/strontium titanate (STO) epitaxial heterostructures and claimed that the conductivity was ionic. I argue that the claimed ionic conductivity lacks experimental support and that the observed conductivity enhancement is most probably due to the p-type conductivity of STO. (1) fabricated yttria-stabilized zirconia (YSZ)/strontium titanate (SrTiO 3 or STO) epitaxial heterostructures on STO substrates, in which YSZ layers with thickness t ranging from 1 to 62 nm were sandwiched between two 10-nm-thick STO layers. They claimed a huge ionic conductivity enhancement in the heterostructures, and the enhancement was attributed to the high oxygen vacancy concentration and the high mobility at the YSZ/STO interfaces. Their major experimental evidence is that the dc conductance was orders of magnitude lower than the ac conductance. However, it should be pointed out that their dc conductance is not purely electronic.A typical cell investigated by García-Barriocanal et al.(1) is Ag/STO 10nm -YSZ 1nm -STO 10nm -STO Substrate /Ag, in which STO is an important part. Nominally undoped STO is almost always doped with acceptor-type impurities. Therefore, it is a mixed conductor of oxygen vacancies and holes. Owing to the higher mobility of holes, nominally undoped STO shows p-type conductivity (2-4). According to the defect chemistry of acceptor-doped STO (2, 3), the p-type conductivity dominates the overall conductivity when the acceptor concentration is low. Therefore, one has to consider the p-type conductivity of the 10-nm-thick STO layers and the STO substrate.The electronic (for example, p-type) partial conductivity can be experimentally deduced by means of the Hebb-Wagner polarization (5, 6). A key point of the Hebb-Wagner polarization is that an electrode should block the ionic species (e.g., oxygen vacancies). Under this condition, the electrical conduction takes place only via the electronic species (e.g., holes) at the steady state. The solubility of oxygen in solid silver is relatively high, and the bulk diffusion of oxygen in Ag is also remarkable (7-9). Therefore, the Ag electrode is not ionically blocking, which is evidenced by the relatively small electrode resistance shown in Fig. 1. In addition, the oxygen diffusion in STO is much too sluggish in the temperature range of 80 to 260°C [the temperature range in figure 3 in (1)]. Estimated from the chemical diffusion coefficient of oxygen in STO (10), it takes about 10 8 s for oxygen to diffuse a distance of only 1 mm at 170°C. Therefore, the dc conduction of the cell Ag/STO 10nm -YSZ 1nm -STO 10nm -STO Substrate /Ag can never reach the steady state within a reasonable time period. In view of the fact that the Ag electrode is not ionically blocking, and that the steady state cannot be reached within a reasonable time period, one can conclude that the dc conductance of the cell Ag/STO 10nm -YSZ 1nm -STO 10nm -STO Substrate /Ag consi...