- Catégorie parente: AST Annales des Sciences et Technologie
Lazhar Mohammedi1, Bahmed Daoudi1, Aomar Boukraa1 and Hadjira Chaib2,1
1Univ Ouargla, Fac. des Mathématiques et des Sciences de la Matière, Lab. Développement des Energies Nouvelles et Renouvelables dans les Zones Arides et Sahariennes, Ouargla 30 000, Algeria
2Univ Ouargla, Fac. des Sciences Appliquées, Département de Génie des Procédés, Ouargla 30 000, Algeria
The stability and electronic structure of orthorhombic hydride TiFeH were investigated using the first principles “fullpotential linearized augmented planewave method” based on density functional theory calculations. We have investigated the lattice parameters, bulk modulus, the electronic structure and the formation energy of the ternary TiFeH hydride in its ground state. The Fermi level of TiFeH hydride falls slightly below that of TiFe. Total and partial DOS analysis reveals that the TiFeH hydride has a metallic characterand the hybridization between iron 3d and hydrogen 1s states appear to be the strongest. The electron density shows that a relatively high electron density extends from the hydrogen atom site to the iron atom site, but not to the titanium atom site which is a very important characteristic in hydrogen storage applications. Its formation energy differs from that in literature.
KEYWORDS:First principles; Density function theory; TiFeH hydride; DOS analysis; Formation energy.
Hydrogen is a clean and renewable fuel for future transportation and energy storage. A promising approach for hydrogen storage is the solid-state storage where H atoms are incorporated in the lattice of the host material. The experimental results of the formation energies of binary metal hydride show that these cover a wide range in stability going from the highly stable hydrides (∆Ef << 0) of the alkali metals, alkaline earth metals, rare earth metals and early transition metals, to the much less stable hydrides of the metals around the middle of the transition metals (∆Ef < 0), and to the unstable hydrides of the late transition metals (∆Ef > 0) . Up to now, none of the binary metal hydrides fulﬁlls both the hydrogen density and the thermodynamic stability criteria. The search for better hydrogen storage and intermediate thermodynamic stability materials continues among the ternary metal hydrides. The intermetallic compound TiFe, which crystallizes in the cubic CsCltype structure  absorbs reversibly up to 1.8 wt% hydrogen to form the orthorhombic TiFeH hydride. Fischer et al.  and Thompson et al.  investigated experimentally TiFeHand found an orthorhombic symmetry for the crystal structure. Many investigations by the DVXα cluster method on TiFe hydrides were carried out in the past [5-9] to determine the metalhydrogen bonding. Gupta studied electronic structure of TiFeH using an augmented plane wave (APW) method where the crystal potential was constructed using Slater’s local exchange approximation . Results were presented on the electronic properties of βTiFeH and compared with the electronic structure of pure TiFe. Kinaci et al. investigated the TiFeH hydride based on a pseudopotential method within the generalized gradient approximation . Formation energy and density of states of TiFeH hydride were calculated. In the present work we have performed first principles DFT electronic calculations of TiFeH using fullpotential linearized augmented plane-wave method (FPLAPW) to determine its structural and electronic properties. We have compared the electronic structure of the TiFeH with the one of pure TiFe. There are some differences with the results found by Gupta in terms of the Fermi level position between TiFeH and TiFe. The calculated formation energy of the ternary TiFeH hydride, which differs from the value obtained by Kinaci et al., is somewhere between those of the two constituent binary hydrides (TiH2 and FeH) satisfying therefore the criterion for hydrogen desorption in PEM fuel cells.
2. Computational details
TiFeH has an orthorhombic structure and a P2221 (17) space group, as shown in Figure 1 . The TiFeH structure is characterized by octahedral framework sites occupied by H atoms of type Ti4Fe2. The atomic coordinates are: titanium in 2d (0.5, 0.757, 0.25), iron in 2c (0, 0.2941, 0.25), and H in 2a (0, 0, 0). All calculations have been done using the full-potential linearized augmented plane wave (FPLAPW) method based on the density functional theory (DFT), as implemented in the Wien2k code . The exchangecorrelation interaction was treated within generalized gradient approximation (GGA) of Perdew et al. . The Kohn-Sham equations are solved selfconsistently by choosing the muffin-tin radii (MT) to be 1.8, 1.8 and 1.3 a.u for Ti, Fe and H, respectively. The core states were treated fully relativistically, while the valence states (3s, 3p, 3d and 4s) were treated within the scalar relativistic approximation. The spinorbit interaction was not included in our calculations. The threshold energy between valence and corestates was -7eV. Taking a convergence energy of 10-4Ry, the RMTKmax and number of kpoint parameters were optimized to be 9 and 3000 kpoints, respectively.
3. Results and discussion
3.1 Structural analysis
By fitting the total energy versus volume data to the nonlinear Murnaghan equation of state , as shown in Figure 2, we obtained the lattice parameters, the value of the bulk modulus and its pressure derivative for both TiFe and TiFeH (Table 1). The equilibrium lattice parameters calculated for TiFe and its hydride TiFeH are close to the available experimental data and previous theoretical calculations, as shown in Table 1.
3.2 Band structure and density of states analyses
As seen from the band structures of TiFe and TiFeH shown in Figure 3, both TiFe and its hydride have a metallic character because of the absence of gap at the Fermi level.The addition of hydrogen atom to the unit cell increases the number of energy bands in first Brillouin zone. Comparing the DOS structure of TiFeH to that of TiFe (Figure 4), we found that the DOS structure of TiFeH shifts slightly towards bonding states at lower energies compared to that of pure TiFe. In the latter, the Fermi level (EF = 0.89624 Ry) falls in a valley of the density of states, characteristic of b.c.c. metals, which separates TiFe bonding from TiFe antibonding manifolds
In the TiFeH hydride, the Fermi level (EF = 0.89394 Ry) falls slightly below that of TiFe whereas Gupta found a shift towards higher energies. We also observe the presence of a structure at low energy, centered at about -8 eV below EF, which results from the metalhydrogen bonding. Figure 5a shows that the contribution of total DOS of Fe dominates in the energy range from - 4 eV to 1 eV which is mostly responsible for structural bonding. Most anti-bonding states are described by total DOS of Ti above the 1 eV. The contribution of total DOS of H is roughly limited to the low energy range from -10 eV to -6 eV. The partial density of states of both Ti and Fe reveals that 3d states density predominates, as shown in Figures. 5-b and 5-c. The hybridization reaction between 3d Fe and 1s H is stronger than 3d Ti and 1s H which is a very important feature of the hydrogen storage compounds (Figures 5-d and 5-e).
3.3 Electron density analysis
According to the contour maps of electron density distributions on TiFeH atomic planes in Fig. 6, we observe that high electron densities extend from the iron atom to the hydrogen atom, but not to the titanium atom. In metal-hydrogen systems, the titanium atom has ordinarily a larger affinity to hydrogen than iron atoms. This confusing result is due to the fact that this kind of chemical bond between iron and hydrogen seems to be one of the important characteristics of the hydrogen storage compounds. Similar results are also found in other hydrogen storage compounds [16, 17].
3.4 Formation energy
Based on the following general reaction equation describing the reaction of H2 gaz with the TiFe alloy:
From the view of thermodynamics, a lower formation energy defined as the total energy difference between the compound and its constituents means better forming ability. The formation energy of TiFe is calculated as:
Where Etot (TiFeH), Etot (TiFe) and Etot (H2) are the total energies of TiFeH, TiFe and H2, respectively. The Etot (H2) taken in this calculation was 2.32 Ry [18-22]. The formation energy of TiFeH is calculated and equals - 45.08 kJ/mol H2. This latter value shows thatthe formation energy of the TiFeH ternary hydride is somewhere between those of the two constituents’ binary hydrides (TiH2, Ef= -76 kJ/mol H2 ) and (FeH, Ef= 15.8 kJ/mol H2 ), and satisfies Ef > -48 kJ/mol H2, the criterion for hydrogen desorption below 100 °C . This criterion is the ultimate goal if hydrogen storage in metal hydrides should be used in conjunction with a polymer electrolyte membrane (PEM) fuel cell. The formation energy obtained by Kinaci et al. was - 21.9 kJ/mol H2, which is less considerably than that in our calculations. In their calculations, the formation energy was not that of absolute value of real formation energy.
The calculated equilibrium lattice parameters of TiFe and its hydride TiFeH are close to the available experimental data and previous theoretical calculations. The TiFeH hydride has a metallic character and the insertion of a hydrogen atom to the unit cell increases the number of energy bands in the first Brillouin zone. The Fermi level falls slightly below that of TiFe whereas Gupta found a shift towards higher energies. Iron is the main contributor to bond formation in the TiFeH hydride, especially with hydrogen. The hybridization reaction between 3d Fe and 1s H is stronger than between 3d Ti and 1s H which is a very important feature for hydrogen storage compounds. The high electron density extends from the iron atom to the hydrogen atom, but not to the titanium atom due to the larger affinity between hydrogen and iron atoms rather than hydrogen and titanium atoms in the TiFeH compound. Therefore, this kind of chemical bond seems to be an important characteristic of hydrogen storage compounds.The formation energy of the TiFeH ternary hydride differs considerably from that obtained by Kinaci et al.. It is somewhere between those of the two constituents’ binary hydride (TiH2 and FeH), and verify Hf > -48 kJ/mol H2, the criterion for possible hydrogen desorption below 100°C in PEM fuel cells.
Smithson H., Marianetti C. A., Van der Ven A., Predith A. and Ceder G.; First principles study of the stability and electronic structure of metal hydrides; Phys. Rev. B 66, 144107-1–144107-10 (2002).
 Thompson P., Reilly J. J. and Hastings J. M.; The application of the Rietveld method to a highly strained material with microtwins: TiFeD1.9; J. Appl. Crystallogr. 22, 256-260 (1989).
 Fischer P., Halg W., Schlapbach L., Stucki F. and Anderesen A.F.; Deuterium storage in FeTi measurement of desorption isotherms and structural studies by means of neutron diffraction; Mat. Res. Bull. 13, 931-946 (1978).
 Thompson P., Pick M. A., Reidinger F., Corliss L. M., Hastings J. M. and Reilly J. J.; Neutron diffraction study of β iron titanium deuteride; J. Phys. F 8, L75–80 (1978).
 Yukawa, H. Matsumura T. and Morinaga M.; Chemical bond state and hydride stability of hydrogen storage alloys; J. Alloys Compds. 293-295, 227-230 (1999).
 Nakatsuka K., Yoshino M., Yukawa H. and Morinaga M.; Roles of the hydride forming and non-forming elements in hydrogen storage alloys; J. Alloys Compds. 293-295, 222-226 (1999).
 Nambu T., Ezaki H., Yukawa H. and Morinaga M.; Electronic structure and hydriding property of titanium compounds with CsCl-type structure; J. Alloys Compds. 293-295, 213-216 (1999).
 Morinaga M., Yukawa H., Nakatsuka K. and Takagi M.; Roles of constituent elements and design of hydrogen storage alloys; J. Alloys Compds. 330-332, 20-24 (2002).
 Yukawa H., Takahashi Y. and Morinaga M.; Electronic structures of hydrogen storage compound, TiFe; Computational Materials Science 14, 291-294 (1999).
 Gupta M.; Electronic structure of FeTiH; J. Phys. F 12, L57-62 (1982).
 Kinaci A. and Aydinol M.K.; Ab initio investigation of FeTieH system; Int. J. Hydrogen Energy 32, 2466-2474 (2007)
 Blaha P., Schwarz K., Sorantin P. and Trickey S.B.;Full-potential, linearized augmented plane wave programs for crystalline systems; Comput. Phys. Commun. 59, 399 (1990).
 Perdew J.P., Burke S. and Ernzerhof M.; Generalized gradient approximation made simple; Phys. Rev. Lett. 77, 3865-8 (1996).
 Murnaghan F.D.; The compressibility of media under extreme pressures; Proc. Natl. Acad. Sci. USA 30, 244 (1944).
 Izanlou A. and Aydinol M.K.; An ab initio study of dissociative adsorption of H2 on FeTi surfaces; Int. J. Hydrogen Energy 35, 1681-1692 (2010).
 Yukawa A., Takashi Y. and Morinaga M.; Alloying effects on the electronic structures of LaNi5 containing hydrogen atoms; Intermetallics 4, 215-224 (1996).
 Takashi Y., Yukawa H. and Morinaga M.; Alloying effects on the electronic structures of Mg2Ni intermetallic hydride; J. Alloys Comp. 242, 98-107 (1996).
 Gunnarsson O. and Johansson P.; The spin-density-functional formalism for quantum mechanical calculations: test on diatomic molecules with an efficient numerical method; Int. J. Quantum Chem. 10, 307 (1976).
 Nakamura H., NguyenManh D. and Pettifor G.; Electronic structure and energetics of LaNi5, αLa2Ni10H and βLa2Ni10H14; J. Alloys Compd. 281, 81-91 (1998).
 Shang C. X., Bououdina M., Song Y. and Guo Z. X.; Mechanical alloying and electronic simulations of (MgH2 + M) systems (M = Al, Ti, Fe, Ni, Cu and Nb) for hydrogen storage; Int. J. Hydrogen Energy 29, 73-80 (2004).
 Son Y., Son Z. X. and Yang R.; Influence of selected alloying elements on the stability of magnesium dihydride for hydrogen storage applications: a first-principles investigation; Phys. Rev. B 69, 094205 (2004).
 Shelyapina M. G., Fruchart D. and Wolfers P.; Electronic structure and stability of new FCC magnesium hydrides Mg7MH16 and Mg6MH16 (M: Ti, V, Nb): an ab initio study; Int. J. Hydrogen energy 35, 2025–2032 (2010).
 Wolwerton C., Ozoliņš V. and Asta M.; Hydrogen in aluminum: First-principles calculations of structure and thermodynamics; Physical Review B 69, 144109-1 (2004).
 Tkacz M.; Thermodynamic properties of iron hydride; Journal of Alloys and Compounds 330-332, 25-28 (2002).
 Harrison K. W., Remick R., Martin G. D. and Hoskin A.; Hydrogen Production: Fundamentals and Cas Study Summaries, Conference Paper NREL/CP-550-47302 January 2010.