We present ab-initio local-density-functional investigations of clean and hudrogen-covered one- (1db) and three-dangling-bond (3db) diamond (111) surfaces, the geometries of the reconstructed surfaces and their stabilities at different values of the hydrogen chemical potential. At low values of the hydrogen chemical potential the clean 1db–(2 × 1) π-bonded Pandey-chain structure forms the ground state. As the hydrogen chemical potential increases, first the hydrogenated 1db–(1 × 1):H structure becomes stable. Then we find a narrow region where a 3db–(2 × 1):2H dihydride surface is stable, until at last a fully hydrogen-saturated 3db–(1 × 1):3H surface has the lowest energy. Then preliminary molecular-dynamics results of reconstruction and graphitization for the 1db surface at elevated temperatures are reported.
Redox potentials of electron transfer reactions are of fundamental importance for the performance and description of electrochemical devices. Despite decades of research, accurate computational predictions for the redox potential of even simple metals remain very challenging. Here we use a combination of first principles calculations and machine learning to predict the redox potentials of three redox couples, $\mathrm{Fe}^{2+}$/$\mathrm{Fe}^{3+}$, $\mathrm{Cu}^{+}$/$\mathrm{Cu}^{2+}$ and $\mathrm{Ag}^{+}$/$\mathrm{Ag}^{2+}$. Using a hybrid functional with a fraction of 25\% exact exchange (PBE0) the predicted values are 0.92, 0.26 and 1.99 V in good agreement with the best experimental estimates (0.77, 0.15, 1.98 V). We explain in detail, how we combine machine learning, thermodynamic integration from machine learning to semi-local functionals, as well as a combination of thermodynamic perturbation theory and $\Delta$-machine learning to determine the redox potentials for computationally expensive hybrid functionals. The combination of these approaches allows one to obtain statistically accurate results.
First-principles calculations for tetragonal zirconia are presented. The stability of the terminations is investigated for different setups (symmetrically or asymmetrically terminated or metal supported) and as function of the film thickness. Several aspects, which are of importance for polar surfaces, are discussed on the basis of the results from the asymmetric setup. Among other things the dielectric constant can be derived from the slab calculations. For the more stable (101) surface a surface phase diagram under hydrogen and oxygen atmosphere is presented. Finally, the interaction between yttrium dopants and the surface is analyzed. While such defects prefer positions far from the surface for a (001) oriented surface, the more stable (101) surface becomes even more stabilized by defects close to the surface. This result is in agreement with experimental findings.
The oxidation of Pd(111) leads to an incommensurate surface oxide, which was studied by the use of scanning tunneling microscopy, surface x-ray diffraction, high resolution core level spectroscopy, and density functional calculations. A combination of these methods reveals a two-dimensional structure having no resemblance to bulk oxides of Pd. Our study also demonstrates how the atomic arrangement of a nontrivial incommensurate surface can be solved by molecular dynamics in a case where experimental techniques alone give no solution.
Over the past few years considerable progress has been achieved in ab initio calculations of the structural, electronic, and dynamic properties of liquid and amorphous systems. The fundamental idea was that the equations of motion for the ionic and electronic degrees of freedom may be integrated simultaneously if the electrons are described by a pseudo-Newtonian dynamics. In metallic systems, the original Car-Parrinello approach fails because a transfer of energy from ions to electrons leads to an increase of electronic kinetic energy so that the electrons drift away from the Born-Oppenheimer surface. An alternative is to calculate the Kohn-Sham ground state of the electrons and the exact Hellmann-Feynman forces at each molecular dynamics step. This calculation is now possible using efficient conjugate-gradient techniques for energy minimization and using a subspace alignment for the prediction of the wavefunctions in new ionic configurations.
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The chemical nature and aggregate state of superheavy copernicium (Cn) have been subject of speculation for many years. While strong relativistic effects render Cn chemically inert, which led Pitzer to suggest a noble‐gas‐like behavior in 1975, Eichler and co‐workers in 2008 reported substantial interactions with a gold surface in atom‐at‐a‐time experiments, suggesting a metallic character and a solid aggregate state. Herein, we explore the physicochemical properties of Cn by means of first‐principles free‐energy calculations, which confirm Pitzer's original hypothesis: With predicted melting and boiling points of 283±11 K and 340±10 K, Cn is indeed a volatile liquid and exhibits a density very similar to that of mercury. However, in stark contrast to mercury and the lighter Group 12 metals, we find bulk Cn to be bound by dispersion and to exhibit a large band gap of 6.4 eV, which is consistent with a noble‐gas‐like character. This non‐group‐conforming behavior is eventually traced back to strong scalar‐relativistic effects, and in the non‐relativistic limit, Cn appears as a common Group 12 metal.
Oxidation is often associated with corrosion, but under the right conditions it can lead to oxide layers which can be applied e.g. as protective layers against corrosion, as insulating layers in microelectronic devices and as catalytic devices[1, 2]. For late transition metals and noble metals (e.g. Pd and Ag), it is now understood that the oxidation proceeds through ultra-thin oxide layers, which are thermodynamically stable at intermediate oxygen potentials and can exhibit astonishing complexity[3–6]. It is still unclear whether the same holds for transition metals and to this end the Rh (111) surface was studied extensively experimentally [7]. To supplement these experimental studies, we performed density functional calculations with the Vienna Ab Initio Simulation Package (VASP) [8] using plane waves and the PAW method [9] as well as generalized gradient approximations [10]. The experimental studies show a Moire like pattern in STM, indicative of a (8×8) oxide layer on a (9×9) supercell of the Rh(111) substrate. This phase is formed at intermediate oxygen pressures, whereas thick corundum-like Rh2O3 is only formed at significantly higher pressures and temperatures. The theoretical calculations indicate that the Moire phase can be rationalised by an ultrathin O-Rh-O trilayer surface oxide. Contrary to the experimental observation, the bulk Rh2O3 oxide is however thermodynamically more stable than ultra-thin layers. This discrepency can be understood by the surface phase diagram shown in Fig. 1(a). It indicates that a single oxygen trilayer on Rh(111) is in fact only metastable, as the trilayer forms only under conditions, where bulk Rh2O3 is already stable (to the right of the thick grey line in Fig. 1(a)). Hence the trilayer is only kinetically stabilised, contrary to the situation on Pd(111) where a Pd5O4 ad-layer is thermodynamically stable for intermediate oxygen potentials [4]. An important hint to the reason of the kinetic stability of the O-Rh-O trilayer is given by the results for the three and four layer thick oxides. Four (three) layer oxides have a lower stability than the single trilayer for oxygen potentials μO <−0.99 eV (μO <−0.78 eV) corresponding to 10 mbar (1 bar) at 800 K. The formation of the bulk oxide must however proceed through thicker oxide layers that present a kinetic barrier for the formation of the bulk oxide at too low chemical potentials. The most favorable structures for 2, 3 and 4 oxygen layers are depicted in Fig. 1(b). In contrast to oxygen atoms on the clean metal, the oxygen atoms at the oxide/metal interface are located preferentially on top of the surface Rh atoms (shifted slightly towards the bridge site). Remarkably, the trilayer termination remains favorable even for thicker oxides. For three oxygen layers (3L) the topmost surface layer contains three Rh atoms, and a fourth single Rh atom is located in the second oxide layer. For four oxygen layers (4L), the trilayer is found at both sides of the oxide, and a single Rh atom interlinks the two O-Rh-O layers. Poster