We present ab initio density-functional calculations for acceptors, donors, and native defects in aluminum nitride, showing that acceptors are deeper (Be ∼ 0.25 eV, Mg ∼ 0.45 eV) and less soluble than in GaN; at further variance with GaN, both the extrinsic donors Si Al and C Al , and the native donor VN (the anion vacancy) are found to be deep (about 1 to 3 eV below the conduction). We thus predict that doped AlN will generally turn out to be semi-insulating in the normally achieved Al-rich conditions, in agreement with the known doping difficulties of high-x AlxGa1−xN alloys. [2,[5][6][7][8], and practically null for InN. Here we contribute to the discussion the results of accurate first principle density functional theory calculations for acceptors, donors, and vacancies in wurtzite AlN. We find that typical candidate acceptors, namely cation-substituting Be and Mg, are moderately but sizably deeper than in GaN. More interestingly, donors known to be shallow in GaN (Si, C, and the nitrogen vacancy) are in fact deep in AlN in their substitutional configuration. Our results are in general agreement with previous results, when comparable. An exception is the behavior of donors, which is at partial variance with previous studies [2,3], but seems to agree with experimental data [1] indicating serious ntype doping difficulties for AlN and high-x Al x Ga 1−x N alloys.Method -We use local-density-functional-theory (LDA) [9] ultrasoft-pseudopotential plane-wave calculations of total energies and forces in doped AlN wurtzite supercells typically encompassing 32 atoms, and with plane wave cutoff of 25 Ry (for further technical details see Refs. [6,7,10]), to predict from first principles the formation energies and thermal ionization energies of cation-substituting Be, Mg, Si, and C, and of the N and Al vacancies in AlN. The carriers concentration at temperature T due to an impurity or defect with thermal ionization energy ǫ, and a formation energy E form , isasssuming impurity incorporation or defect creation in thermal equilibrium at a growth temperature of T g , and with N s =2.44×10 22 cm −3 available cation or anion sites (i.e. half the theoretical atomic density of AlN). Thus, the largest the formation and ionization energies, the less efficient the doping. A non-zero formation entropy (neglected here) will of course enhance the dopant concentration. The formation energy for an impurity in charge state Q is (2) with µ e the electron chemical potential (synonimous with the Fermi energy E F in our T=0 calculations), E tot (Q) the total energy of the fully-relaxed defected supercell in charge state Q, E Q v its top valence band energy, n X and µ X the number of atoms of the involved species (X=Al, N, impurity) and their chemical potentials. The latter potentials are determined by the equilibrium conditions with AlN and the compounds (if any) of the specific impurity with Al or N. The structures and formation enthalpies of the solubility limiting compounds (Al 2 O 3 , Si 3 N 4 , Be 3 N 2 , Mg 3 N 2 , and d−C) are calc...