Recent technical advances in scanning transmission electron microscopy (STEM) and x-ray detector technology have made it possible to do atomic-resolution chemical mapping using energydispersive x-ray spectroscopy (EDS). So far, most of these efforts have been applied to materials such as perovskite oxides [1][2][3], e.g. SrTiO 3 , and compound semiconductors [4,5], which have well-known crystal structures with relatively large lattice spacings, that are also comparatively resistant to electronbeam irradiation. This radiation-resistant property allows longer dwell times at each recording point (i.e., pixel) for achieving the signal-to-noise (S/N) ratio that is necessary for elemental mapping. For the study of intermetallics such as body-centered-cubic (bcc) alloys that have small interatomic distances and are relatively sensitive to the electron radiation, improvement in the spatial resolution as well as reduction in the overall electron dose are required. In this work, we report our strategy to overcome these difficulties as well as applications of the techniques for quantification of chemical composition at the lattice sites in intermetallic bcc alloys [6].In chemical mapping, the shortest lateral distance between columns of identical atoms in a crystal projection determines the required spatial resolution necessary for resolving the atomic columns [6, 7]. The required spatial resolution is 3.9 Å for SrTiO 3 in the [001] direction and about 3.5 Å for GaAs in the [110] direction. The smaller dimensions of the unit cell (~2.9 Å) for bcc intermetallic alloys require higher spatial resolution. This improvement can be achieved by a combination of small electron probe (<1.5 Å), using a thin TEM specimen (< 20 nm) and improving the S/N ratio through averaging of EDS maps that are related to each other via lattice-vector translations in the image plane (for convenience, we have termed this process "lattice-averaging"). Significant improvement in the S/N ratio of EDS mapping can be achieved by lattice-averaging (Fig.1), which compensates for reduction in X-ray count due to the selection of small electron probe and thin specimen, and also leads to an overall reduction of electron dose necessary for EDS mapping [6]. By choosing a thin TEM specimen, the EDS signal is localized to atomic columns [1,3, 6, 7] and X-ray counts from individual atomic columns can be approximated by a Gaussian distribution. The width of the Gaussian peak is then effectively determined by convoluting the electron probe with the effective EDS local ionization potential, leading to a spatial resolution of better than 2.0 Å [6]. Fig.2 shows EDS maps of Fe Κα and Co Κα, obtained from a Fe-Co alloy, showing an ordered bcc structure with the Fe and Co atoms preferentially occupying the A-sites and B-sites in the bcc lattice [6]. Furthermore, the chemical composition at the atomic column positions can be quantified column-by-column using the Cliff-Lorimer method [6][7][8][9].