The Structures and Properties of Y-Substituted Mg2Ni Alloys and Their Hydrides: A First-Principles Study

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Received 11 December 2015; accepted 22 January 2016; published 25 January 2016

1. Introduction

Due to rich reserves in the earth’s crust, high hydrogen capacity (3.6 wt%), light weight and low cost, Mg_{2}Ni- type alloy hydrides remain as attractive hydrogen storage materials [1] [2] . However, the practical application of the alloy materials has not been achieved because of unfavorable thermodynamics, poor hydrogenation/dehy- drogenation kinetics and releasing undesirable by-products [3] .

Many researches have been devoted to overcoming these drawbacks and improving the properties of hydrogen storage via modifying microstructure by mechanical alloying [4] , alloying with other elements [5] [6] , adding catalysts [7] and composite structures [8] . The effects of transition metals including Cu, Co, Mn, Y, Ti, N band Crelements [9] -[12] on the hydrogen storage properties of Mg-based metal hydrides are investigated and discovered that the properties of hydrogen storage are improved by alloying with a small amount of transition metals in different degrees.

It is believed that alloying of Mg_{2}Ni with transition metals is beneficial to improve the hydrogenating and dehydrogenating kinetics. The electronic structure of element Y is 4d^{1}5s^{2} and it can be incorporated into the metal boride. In addition, its chemical properties and physical performance are similar to La which can be used as an alloy element for hydrogen storage. The density and cohesive energy of Y atom are also relatively small. Therefore, Y has great potential to improve the performance of Mg_{2}Ni alloy and its hydride. Kalinichenka et al. [13] studied that Y can be solved in Mg_{2}Ni and the Mg-Ni-Y alloy exhibits higher dehydrogenation rates comparing with that of the Mg-Ni alloy. Song et al. [14] reported the microstructure and the hydrogenation properties of melt-spun Mg_{67}Ni_{33−x}Y_{x} alloys and found that the hydrogen storage capacity and kinetics of Mg_{2}Ni are improved with Y doping. Zhang et al. [15] investigated that the substitution of Y for Mg had an insignificant effect on the activation ability of the Mg_{2}Ni-type alloys, but it dramatically improved the cycle stability of the as- milled alloys. These experiments proved that Y plays an important role in improving the properties of Mg_{2}Ni alloy for hydrogen storage. Thus, my understanding is that, alloying of Mg_{2}Ni with Y can be expected to improve some performances of hydrogen absorption/desorption capacity and kinetics significantly.

In recent years, a number of theoretical investigations about the doped/substituted complex hydrides using first-principles calculations have been reported [16] -[19] . A first-principles study on the structures and properties of hydrogen storage alloy Mg_{2}Ni, of aluminum and silver substituted alloys Mg_{2−x}M_{x}Ni (M = Al and Ag), and of their hydrides Mg_{2}NiH_{4}, Mg_{2−x}M_{x}NiH_{4} was performed by Zeng et al. [20] . Their results show that the hydrogen storage capacity is decreased by the substitution and the substitution destabilizes the hydrides. However, there are no available theoretical reports about the structures and properties of Y substituted Mg_{2}Ni alloys and their respective hydrides to the authors’ knowledge. The models are new for the materials to store hydrogen.

We focus primarily on the stable configuration of Mg_{2}Ni alloys with Y substitution and determine the optimum position of Y. Furthermore, the energies, enthalpies of formation and electronic structures of Y alloying Mg_{2}Ni and its hydrides are also calculated and analyzed using a first-principles plane-wave pseudo potential simulations based on the density functional theory in this paper. These simulations are beneficial to improve our understanding of the effects of substitution on the properties of Mg_{2}Ni, and of the design about advanced magnesium-based hydrogen storage materials.

2. Computational Details

2.1. Computational Model

The crystal structure of Mg_{2}Ni is hexagonal and its space group is P6_{2}22 (No.180) [21] , as shown in Figure 1(a). The lattice constants of Mg_{2}Ni are a = b = 5.205 Å, c = 13.236 Å, α = β = 90˚, γ = 120˚. There are 12 Mg and 6 Ni atoms existing in the unit cell of Mg_{2}Ni. The spatial positions Mg and Ni atoms are respectively 6f(0.5, 0, 0.1187), 6i(0.16, 0.324, 0) and 3b(0, 0, 0.5), 3d(0.5, 0, 0.5). Single Y atom substituting for Mg and Ni atoms are investigated respectively. Moreover, it has been shown that Mg_{2}NiH_{4} forms readily by hydrogenating the alloy Mg_{2}Ni [22] . The space group of Mg_{2}NiH_{4} is monoclinic C2/c (No.15) and the lattice constants are a = 14.343 Å, b = 6.404 Å, c = 6.483 Å, β = 113.52˚, as shown in Figure 1(b). 16 Mg, 8 Ni and 32 H atoms are in the unit cell of Mg_{2}NiH_{4} where Mg occupying the 8f, 4e, 4e sites and Ni the 8f site and H the 8f, 8f, 8f, 8f sites [23] [24] . The new systems of Y alloying Mg_{2}NiH_{4} are studied.

2.2. Computational Method

All the density-functional theory (DFT) calculations are performed using a plane-wave basis set with the projector augmented plane wave (PAW) method as implemented in the Vienna ab initio simulation package (VASP)

Figure 1. Structures of (a) Mg_{2}Ni, (b) Mg_{2}NiH_{4}, (c) Mg_{15}YNi_{8}H_{32} (where green, purple, red and orange balls denote Mg, Ni, H and Y atoms, respectively).

[25] - [27] . Projector Augmented Wave (PAW) potentials are used to treat the core-valence interaction [28] . The PW91 [29] [30] generalized gradient approximation (GGA) is employed for the exchange-correlation functional. The electronic wave functions are expanded by plane waves with a kinetic energy cutoff of 350 eV to attain the required convergence. All of the self-consistent loops are iterated until the total energy difference of the systems between the adjacent iterating steps is less than 10^{−7} eV. The Brillouin zone is sampled by 6 × 6 × 2 mesh points in k-space based on Monkhorst-Pack scheme [31] for all systems. The valence electrons of 1s for H, 2p and 3s for Mg, 3p, 3d and 4s for Ni, and 4d and 5s for Y are considered in the calculations.

3. Results and Discussions

3.1. The Structure of Substituted Mg_{2}Ni by Y

In order to check the accuracy of the calculations, we first optimize the structure of Mg_{2}Ni alloy and its hydride and compare the calculated lattice parameters with those determined experimentally. Then we consider the substitution of Mg and Ni by Y in independent spatial positions respectively. To single out a scenario that is most likely responsible for the stabilization of the crystal structure, the lattice parameters and enthalpies of formation ΔH for each case are calculated. The ΔH is calculated by taking the difference in total electronic energy of the products and the reactants [32] :

(1)

In the case of the crystal structure which including xMg, yY, zNi, the enthalpies of formation are calculated by the following equation:

(2)

where refers to the total energy of substituted Mg_{2}Ni by Y.

, and are the energy of every atom in HCP Mg, HCP Y and FCC Ni crystals, respectively. x, y, z are the numbers of Mg, Y and Ni atoms, respectively. Through the calculation, the values of, and are −1.595, −6.379 and −5.415 eV, respectively.

Table 1 displays the volume, lattice constant, total energy and enthalpies of formation of all the structures including Mg_{2}Ni, substituted Mg_{2}Ni by Y and their hydrides. The lattice constants of Mg_{2}Ni after geometry optimization are a = b = 5.180 Å, c = 13.232 Å, which agree well with the experimental data a = b = 5.205 Å, c = 13.236 Å [21] . The enthalpy of formation of Mg_{2}Ni is −3.211 eV, which means that the unit cell of Mg_{2}Ni is −51.612 kJ/mol. It is very close to the experimental values −51.9 kJ/mol [33] . When Y atom is added into Mg_{2}Ni, all the volumes of crystal structures will increase compared with the original structures. Moreover, it can be clearly observed that when the position of Mg (6f) is occupied by Y atom in Mg_{2}Ni, the total energy and the enthalpy of formation are the minimum. It indicates that the structure of Mg_{11}Y(6f)Ni_{6} has the optimal stabilization among all the substituted structures.

Table 1. Volume, lattice constant, total energy, enthalpy of formation of Mg_{2}Ni, Y-substituted Mg_{2}Ni and their hydrides.

3.2. The Properties of Substituted Mg_{2}NiH_{4} by Y

Based on the stable structure of Mg_{11}Y(6f)Ni_{6}, we study the properties of substituted Mg_{2}NiH_{4} by Y. Firstly, We have proved that the theoretical lattice constants and internal atomic positions of Mg_{2}NiH_{4} are in good agreement with experimental results [23] . The states are displayed in Table 1. Various substitutive positions of Mg are considered. We find that the total energy of each new structure is very close. Thereby, a reasonable structure Mg_{15}YNi_{8}H_{32} is selected to be investigated in detail, as shown in Figure 1(c).

In order to research the effects of Y on the properties of Mg_{2}NiH_{4}, We calculate the enthalpies of formation of Mg_{2}NiH_{4} and Mg_{15}YNi_{8}H_{32} respectively. In general, the formation of Mg_{2}NiH_{4} can be expressed by the following reaction:

(3)

The enthalpy of formation of Mg_{2}NiH_{4} can be expressed in Equation (4):

(4)

In the same way, the reaction of formation and the enthalpy of formation of Mg_{15}YNi_{8}H_{32} can be respectively written as Equations (5) and (6):

(5)

(6)

where, , and are the total energy of Mg_{2}NiH_{4}, Mg_{2}Ni, Mg_{15}YNi_{8}H_{32} and Mg_{11}Y(6f)Ni_{6}, respectively.

is the energy of free H_{2} molecule. The calculated results are also shown in Table 1. For pure Mg_{2}NiH_{4}, the enthalpy of formation is −64.667 kJ/mol which coincides closely with the experimental result −64.4 ± 4.2 kJ/mol reported by Reilly et al. [22] . Furthermore, the enthalpy of formation of Mg_{15}YNi_{8}H_{32} is −62.554 kJ/mol which is higher than that of pure Mg_{2}NiH_{4}. It can be clearly seen that the introduction of Y atom has effects on the destabilization of Mg_{2}NiH_{4} in terms of energy. This is energetically favorable to perform the dehydrogenation reaction of substituted Mg_{2}NiH_{4} by Y.

To make further investigation about the performance of dehydrogenation, we calculate the energies of Mg_{2}NiH_{4} and Mg_{15}YNi_{8}H_{32} which dissociate the nearest 2 H atoms around Ni atoms. The dehydrogenation energy is calculated by Equation (7):

(7)

The results are shown in Table 2. From Table 2 we can see that the addition of Y clearly decreases the dehydrogenation energy of Mg_{2}NiH_{4} by about 47% to 0.983 eV. It suggests that although Y atom has poor effects on the destabilization of Mg_{2}Ni, it breaks down the stability of Mg_{2}NiH_{4} positively and improve the dehydrogenation kinetics of Mg_{2}NiH_{4} which as one of the hydrogen storage materials.

3.3. Electronic Structure

In order to further understand the effects of Y atom on the dehydrogenation properties of Mg_{2}NiH_{4} alloy, the electronic properties of Mg_{2}Ni and Mg_{15}YNi_{8}H_{32} are studied by calculating total density of states (DOS) and partial density of states (PDOS). Figure 2 displays the DOS and PDOS of Mg_{2}Ni and Mg_{15}YNi_{8}H_{32} alloys.

Form Figure 2(a) we can see that there are two main peaks in total density of states below Fermi level. The bonding electron of the energy region between −9.2 and −3.7 eV is mainly dominated by Hs, Nis and Nid orbits, partial Mgs orbit. It is implied that H atoms tend to bond with Ni rather than Mg atoms in the structure of Mg_{2}NiH_{4}. The result is in correspondence with the conclusion that the interaction Ni-H is stronger than that of Mg-H which studied by Jasen [34] . There is a major contribution with Ni p, Ni d and Mg s orbits in the region from −2.4 eV to Fermi level. This indicates that Mg and Ni atoms have hybridization which keeps the structure of Mg_{2}NiH_{4} stable. In addition, Ni d orbit plays the dominating role in the bonding electron.

Table 2. Calculated dehydrogenation energies of Mg_{15}MNi_{8}H_{32} (M = Mg, Y) (eV).

(a) (b)

Figure 2. Total density of states and partial density of states of (a) Mg_{2}NiH_{4}, (b) Mg_{15}YNi_{8}H_{32}.

Compared to pure Mg_{2}NiH_{4}, the enthalpy of formation and dehydrogenation energy change markedly due to the substituted Mg_{2}NiH_{4} by Y. Figure 2(b) displays that below Fermi level Mg_{15}YNi_{8}H_{32} has two main bonding peaks from −10.7 to −5.2 eV and −4.1 to −1.6 eV. It is not difficult to find that all the bonding peaks in total density of states move to the energy of deep potential well and the number of bonding electron reduces comparing to Mg_{2}NiH_{4}. It demonstrates that the substitution of Y alloying weakens the interaction of the atoms and destabilizes the structure of the hydride. The effects of Yd orbit on the bonding electron are significant especially for the energy region from −4.1 to −1.6 eV. What is more, Yp and d orbits contribute to the bonding electron and have mutual interaction with Nip and d orbits. It is also worth noting that the overlapping region between Nid and Hs orbits decreases obviously. It means that the interaction between Ni and H atoms become weak.

4. Conclusion

We have investigated the structure and properties of substituted Mg_{2}Ni alloys by Y and the corresponding hydrides. The structure parameter, enthalpy of formation, dehydrogenation energy and electronic structure are calculated by the first-principles method based on density functional theory in this paper. Through analyzing the simulation results, we can draw the conclusions that when Y atom occupies the Mg(6f) lattice site, the structure of Mg_{2}Ni is the optimal stable. The substitution of Y destabilizes the stability of Mg_{2}NiH_{4} and decreases the dissociated energies of H atoms due to the Ni-H bond weakened by Y. Therefore, the method of substitution is in favor of the dehydrogenation reaction for Mg-based hydrides as hydrogen storage materials. Moreover, we will continue to perfect this respect, for instance, whether the effect of Y elements in the case of different numbers of Y metals and different substituents will change.

Acknowledgements

This work was supported by Innovation Program of Shanghai Municipal Education Commission, China (10YZ172) and Subjects Construction Program of Shanghai University of Engineering Science, China (2012gp43) and Graduated Innovative Research Project of Shanghai University of Engineering Science (E1-0903-14-01107- 14KY0411).

NOTES

^{*}Corresponding author.

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