Characteristics of A2B7-type LaYNi-based hydrogen storage alloys modified by partially substituting Ni with Mn
Graphical abstract
Introduction
Intermetallic compounds RMn (R = rare earth; M = transition metal; 1 ≤ n ≤ 5) can reversibly store a large amount of hydrogen and are therefore important energy storage materials [1], [2], [3]. According to the LaNi binary phase diagram [4], phases such as RNi3 and R2Ni7 may form during heating through peritectic reactions. Among the RNi3-type compounds (R = La, Ce, Pr, Nd, Sm, Gd, Tb, Dy, Ho, Er, Y), YNi3 exhibits the largest cell volume, lowest density, and most satisfactory electrochemical characteristics [5].
The partial substitution of Y in YNi3 compounds with La and/or Ce leads to the formation of ternary yttrium-based alloys having the general formula La1−xCexY2Ni9 (0 ≤ x ≤ 1) [1], [6], [7], [8]. Similar to the R–MgNi system superlattice alloys [9], these R–YNi compounds adopt a rhombohedral structure of the PuNi3 type, which can be described as an intergrowth between RNi5- and RNi2-type structures and induces greater receptivity to hydrogen than commercial RNi5-type alloys. Furthermore, the Y element and Mg element have similar effects in the two series of hydrogen storage alloys. Both Mg in the LaMgNi alloy and Y in the LaYNi alloy increase the structural stability of the corresponding alloys in the hydrogenation/dehydrogenization process and avoid or delay the hydrogen-induced amorphous (HIA) of the alloys [10], [11], [12]. The lanthanum compound LaY2Ni9 absorbs 12.3 H/f.u. (formula unit), which corresponds to 380 mAh g−1 in equivalent electrochemical units under 1 bar of hydrogen gas, and its plateau pressure for absorption is 0.06 bar at 298 K [1]. Owing to these characteristics, ternary yttrium-based alloys are among the most promising negative electrode materials for metal hydride–nickel (MH–Ni) batteries.
In recent years, R–MgNi system hydrogen storage alloys have been investigated extensively, and their discharge capacities have been found to be as high as 414 mAh g−1 [13], [14], [15], [16], [17], [18], [19], [20], [21], [22], [23], [24], [25], [26]. However, the relatively high volatility of Mg makes the preparation process difficult and expensive [14], [18], [19], [20], [21], thereby restricting the application of this family of alloys. In contrast, R–YNi alloys can be easily prepared by induction melting, which is also preferable for R–MgNi alloys. However, the discharge capacity of the AB3-type LaYNi alloy is only 260 mAh g−1 [6], [7], [8], which requires further enhancement. In our previous work [27], [28], [29], we found that the electrochemical properties of AB3-, A2B7-, and A5B19-type R–YNi system alloys can be improved significantly by adjusting the alloy composition using the method of element substitution. The partial substitution of Ni by metals such as Mn and Al can significantly increase the discharge capacity of the alloys and provide an optimal trade-off between high hydrogen capacity and good cyclic stability.
Mn is an indispensable element in conventional mischmetal-based AB5-type alloys for maintaining cycle stability and high-rate dischargeability (HRD) [30]. Nevertheless, the substitution of the Ni in the mischmetal-based superlattice alloys by Mn decreases both the gaseous phase and electrochemical capacities due to a reduction in the abundance of the main A2B7 phase. It additionally adversely affects alloy properties such as the phase homogeneity, capacity, cycle stability, HRD, and surface reaction due to deterioration in the surface catalytic ability as the Mn content increases [30]. However, the R–MgNi system superlattice alloy family (AB3, A2B7, A5B19) tends to focus on La- and Nd-only alloys, for which the partial substitution of Mn for Ni can increase the lattice parameters and the cell volume, decrease the plateau equilibrium pressure, increase the discharge capacity and improve the electrochemical catalytic activity of the alloys [22], [23], [24]. In practice, there exists an optimum content of Mn for improving the hydrogen storage property and overall electrochemical properties of the alloys. Mn might be suitable for dual tuning of the thermodynamic and kinetic properties of the Mn-containing hydrogen storage alloys [31].
A study of the effect of the partial substitution of Ni by Mn on the structure and properties of the A2B7-type LaY2Ni10.5 superlattice alloy is therefore necessary and is presented in the present work.
Section snippets
Experimental
The alloys designed as A2B7-type LaY2Ni10.5−xMnx (x = 0.0, 0.5, 1.0, 2.0) were prepared under a 0.05 MPa argon atmosphere in a vacuum induction-quenching furnace with a copper wheel rotating at a linear velocity of 4.33 m s−1. The purities of the component metals were at least 99 wt %. An appropriate excess (2 wt % La, 2 wt % Y and 5 wt % Mn) of some component metals were added to compensate for evaporative loss. The chemical compositions of the alloys were examined by inductively coupled
Phase structure
Fig. 1 shows the Rietveld refinement of the XRD profiles of the LaY2Ni10.5−xMnx (x = 0.0, 0.5, 1.0, 2.0) alloys. The phase abundance, cell parameters, and internal strain are listed in Table 1. All the alloys have multiphase structures composed of Gd2Co7-type (3R) and Ce2Ni7-type (2H) phases; in addition, the x = 0.0 alloy contains a small amount of the Ce5Co19-type (3R) phase (2.04%) and a very small amount of the PuNi3-type (3R) phase (1.38%). As the Mn content increases, the abundance of the
Conclusions
- (1)
The A2B7-type LaYNiMn alloys investigated in our study constitute a system of new hydrogen storage materials. LaY2Ni10.5−xMnx (x = 0.0, 0.5, 1.0, 2.0) alloys consist of Gd2Co7- and Ce2Ni7-type phases. With the addition of Mn, the abundance of the Ce2Ni7-type phase increases from 44.74% (x = 0.0) to 76.97% (x = 2.0). The lattice parameters and cell volumes of both the Gd2Co7- and Ce2Ni7-type phases increase with increasing x. The internal strains show a decreasing tendency with increasing x.
- (2)
The
Acknowledgments
This work was supported by the Key International Science and Technology Cooperation Projects of the Ministry of Science and Technology of the PRC (2010DFB63510, 2013DFR50940) and the National Nature Science Foundation of China (51061001).
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