Using first-principles total-energy methods, we calculate the formation energy for typical Mn defects in bulk Si and Ge and on (001) surfaces, from which the various Mn solubility limits are derived. Applying the theory for ultrahigh doping in semiconductors, we can understand why Mn solubility in epitaxially-grown Si and Ge films could be several atomic percent while the solid solubility limits are many orders of magnitude smaller. In particular, we suggest that hydrogen passivation of the surface during growth could be the key to such high solubilities.The recent study of ferromagnetic properties of transition metal doped III-V semiconductors have rekindled interest in dilute magnetic semiconductors. 1,2 Among the recent developments, it was shown that germanium 3 and silicon 4,5 can also be doped to a high Mn concentration, making them good candidates for spintronic applications. For example, using gas-source molecular beam epitaxy (MBE) on a Si͑001͒ substrate, up to 5 atomic percent Mn has been successfully incorporated into thin Si films at 300°C. 4 The internal magnetization of local Mn spins have also been observed by Hall measurement. Since Si is the backbone of the electronic industry, it is utterly important to develop group-IV based spintronics as integration with existing silicon technologies would be straightforward. Interestingly, however, the Mn solubility in these materials exceed far beyond the solid solubility limits, determined experimentally. 4 This raises the interesting question as to how such high solubility could be achieved. It is likely that epitaxial growth has an impact on the Mn incorporation. Without knowing the microscopic mechanism, however, it will be difficult, if not irrelevant, to predict the magnetic properties of the epitaxially grown thin films.In this paper, using first-principles total energy calculations, we have studied the Si: Mn and Ge: Mn systems. We find that for Si, Mn prefers the tetrahedral interstitial site in the bulk but substitutional site at (001) surfaces. For Ge, Mn prefers the interstitial site both in bulk and at surfaces. The differences in the defect types between Si and Ge can be explained in terms of the difference in the vacancy formation energy. Our calculated solid solubility limit for Si is in good agreement with experiment. Surface enhanced kinetic solubility limits were also considered but fall far short of the experimental values. We suggest instead that surface passivation, e.g., by hydrogen in gas-source MBE, could be the primary reason for the significantly enhanced Mn solubility in Si beyond the solid solubility limit.The calculations were performed using the densityfunctional theory within the generalized gradient approximation (GGA). 6 We used the Vanderbilt ultrasoft pseudopotentials 7 and the Vosko-Wilk-Nusair interpolation for the correlation functional in the spin-polarized calculations, as implemented by the plane-wave total energy VASP code. 8 The cutoff energy for the planewave expansion is 270 eV. For bulk defect calculations, we ...