Cycling stability of La-Mg-Ni-Co type hydride electrode with Al

   SUN Xian-zhong(孙现众), PAN Hong-ge(潘洪革), GAO Ming-Xia(高明霞)， LI Rui(李 锐),LIN Yan(林 燕),L MA Shuai(马  帅,)

Department of Materials Science and Engineering, Zhejiang University, Hangzhou 310027, China

Received 12 May 2005; accepted 12 September 2005

Abstract: The reason for the improvement of the cycling stability of the La-Mg-Ni-Co based hydrogen storage alloy electrode was also systematically investigated. It is found that the cell volume expansion of upon hydrogenation is obviously decreased after Al partial substitution for forNi,and a subsequent decrease in the pulverization of the alloy particlesis, which leads to the decrease of the rate of contact of the fresh alloy surface with alkaline electrolyte and the increase of the charge/discharge efficiency. Moreover, the occurrence of Al in the alloy can create a dense Al oxide film during charge/discharge cycling. This dense oxide film can prevent further oxidation of the active components in the alloy, which is believed to be the most important reason responsible responsiblefor the improvement of the cycling stability of the La-Mg-Ni-Mn-Co-Al type alloy electrodes.

Key words: Hydrogen Ni/MH batteries; Li-Mg-Ni-Co based alloy; storage alloys; Cycling stability; Al substitution

1 Introduction

Recently, a new type R-Mg-Ni (R= rare earth or Ca element) system hydrogen storage alloys with high hydrogen storage capacity has been studied and reported [1－13]. Kadir et al[1－3] found that the maximum hydrogen storage capacity of the (La_0.65Ca_0.35)(Mg_1.32Ca_0.68)Ni₉ alloy reached 1.87% (mass fraction, the same below if not mentioned), and that of the (Y_0.5Ca_0.5)(MgCa)Ni₉ alloy went up to 1.98 %. Meanwhile, it is also reported that some of the R-Mg-Ni based alloys exhibited promising electrode properties[4－13]. For example, the La-Mg-Ni-Co system AB_3-3.5 type alloys were found to have high discharge capacity of 387－410 mA·h/g[4]. Moreover, PAN and LIU et al[5, 6] studies the structure and electrochemical properties of La_0.7Mg_0.3(Ni_0.85Co_0.15)_x (x=2.5-5.0) alloys,and found that the alloy － with x=3.5 had a maximum discharge capacity of 395.6 mA·h/g and good electrochemical kinetic properties. In addition, the proper heat treatment or the partial substitution of Mn for Ni could improve the overall properties of the La-Mg-Ni-Co type electrode alloys[8－13]. Especially, the cycling stability of the La-Mg-Ni-Co alloy could be obviously improved by the addition of Al, but the mechanism still has not been clearly elucidated.

In this paper, in order to reveal the effect of Al on the electrochemical properties and microstructures of La-Mg-Ni-Co type alloys, the La_0.7Mg_0.3-Ni_2.65－x- Mn_0.1Co_0.75Al_x (x=0, 0.3) alloy electrodes was selected and studied by XRD, SEM and AES measurements during their electrochemical cycling.

2 Experimental

La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) were prepared by vacuum induction levitation melting on water-cooled copper crucible under argon atmosphere.   were usedThe alloy ingots were turned over and remelted twice for homogeneity. Then, part of the alloys were mechanically crushed and ground into the powder with size of less than 47 μm.

Two kinds of test electrodes were prepared. One was by cold pressing 400 mg pure alloy powder up to a pressure of 20 MPa. The other one was prepared by cold pressing a mixture of 100 mg alloy powders and 400 mg carbonyl nickel powders up to a pressure of 16 MPa. The mixture electrode was only used in the test of discharge capacity. Each alloy pellet was then interposed between two foamed Ni plates (55 mm×20 mm), the outer rims of which were tightly spot-welded to keep a sufficient contact with the foamed Ni plates. Electrochemical measurements were conducted in a standard tri-electrode cell consisting of a working electrode (MH electrode), a sintered Ni(OH)₂/NiOOH counter electrode and a reference electrode of Hg/HgO, and a 6 mol/L KOH solution was used as electrolyte. Each electrode charged at 60 mA/g for 7 h followed by a 10 min intermission, subsequently being discharged at 60 mA/g to the cut-off potential of －0.6 V (vs Hg/HgO).

After a certain number of charging/discharging cycles, the electrodes were taken out and then washed with distill water followed by drying in vacuum. To investigate the difference of the crystal structure, surface morphology and concentration profiles of the degraded electrodes before and after cycling after charging/discharging cycles, XRD (ARL, Cu K_α, 45 kV, 40 mA), SEM(Hitachi S-4700, FESEM) and AES(PHI-550, 3 kV, 10 μA) were performed, respec- tively. The electrode surface was sputtered with Ar⁺ on an area of 1.5 mm×1.5 mm at at 4 kV and 15 mA.

3 Results and discussion

Fig.1 shows variation of the discharge capacity of the La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) alloy electrodes vs cycle number at 303 K. It can be seen that the cycling stability of the alloy electrode with Al (x=0.3) was markedly improved compared with that of the alloy without Al. After 100 charge/discharge cycling, the discharge capacity retention (C₁₀₀/C_max) of the alloy electrodes increased from 32.0% (x=0) to 73.8% (x=0.3), which is very considerablybeneficial to the practical application of the La-Mg-Ni-Co type hydrogen storage electrode alloy in the Ni/MH secondary batteries thongh the initial discharge capacity decreased from about  400 to 350 mA.h/g. 

Fig. 1 Discharge capacity vs. cycle numbers of the La_0.7Mg_0.3Ni_2.65-xMn_0.1Co_0.75Al_x (x=0, 0.3) alloy electrodes at 303 K

Fig.2 shows the XRD patterns of the La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) alloys after charging. In previous works[14], it has been reported the La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) as-cast alloys mainly consist of the (La,Mg)Ni₃ phase and LaNi₅ of (La,Mg)Ni₃ and the LaNi₅ in the above alloys still maintain the rhombohedral PuNi₃-type structure and hexagonal CaCu₅-type structure, respectively. Moreover, phase. From Fig.2, it can be seen that the hydride phases It should be noted that the diffraction peaks for the hydride phase of the alloy with Al move toward  angles compared with the alloy without Al, which implies that the cell volume expansion upon hydrogenation decreases after the partial substitution of Al for Ni. Table 1 lists the lattice parameters and unit cell volumes of the hydride phases of the (La,Mg)Ni₃ phase and the LaNi₅ phase. It can be seen that the cell volume expansion ratio (?V/V) of the  (La, Mg)Ni₃-H phase decreases from 19.58% to 14.38%, and that of the LaNi₅-H phase decreases from 18.62% to 15.13%. This phenomenon indicates that the alloy with Al can undergo a smaller cell volume expansion and contraction during the charge/discharge cycling process and a subsequent lower pulverization of the alloy particles. Thus, the oxidation/corrosion of the active constituents in the alloys decreases and the electric conductivity increases, which leads to the improvement of the cycling stability of the alloy electrodes.

Fig. 2 XRD patterns of the La_0.7Mg_0.3Ni_2.65-xMn_0.1Co_0.75Al_x (x=0, 0.3) alloys after charging. _－: (a) x=0.3; (b) x=0

Fig.3 shows the SEM micrographs of the La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) alloys before and after cycling. As can be seen from Fig.3, with increasing cycle number, the alloy particles are gradually pulverized due to the cell volume expansion and contraction during charging/discharging cycles. Further more, it can also be seen that the particle size of the alloy with Al is larger than that of the alloy without Al under the same condition. This result indicates that the process of the pulverization is inhibited and the rate of pulverization is decreased by the partial substitution of Ni by Al. In addition, it can be seen that the surface is very fresh and activated for the as-cast alloys. After electrochemical charge/discharge cycling, the particle surface becomes rough, and a passive layer forms. However, the oxidation/corrosion progress of the active components is obviously inhibited after partial substitution of Ni by Al. It is very obvious that, after 80 cycles, the surface of the alloy without Al has been fully covered by the passive layers (Fig.3(c)), but, the grey alloy matrix can be clearly observed for the alloy with Al as shown in Fig.3(f), which is also one of the reasons of the improvement of the cycling stability of the alloy electrode after the partial substitution of Al for Ni.Fig.4-5 shows the AES profiles of the La_0.7Mg_0.3Ni_2.65－xMn_0.1Co_0.75Al_x (x=0, 0.3) alloy electrodes before and after cycling. For the alloy without Al, it can be seen that the oxygen content on the    alloy surface increases with cycling, which indicates that the oxidation/corrosion of the alloy components becomes more and more serious during the charge/discharge cycling process. However, in the case of Ni being partially substituted by Al, the oxygen content on the alloy surface is only slightly changed., which implies that the oxidation/corrosion of the active components of the alloy is effectively inhibited. From

Table 1 Characteristics of hydride phases in the L La_0.7Mg_0.3Ni_2.65-xMn_0.1Co_0.75Al_x (x=0, 0.3) hydrogen storage alloys.

Fig. 3 SEM micrographs of the La_0.7Mg_0.3Ni_2.65-xMn_0.1Co_0.75Al_x (x=0, 0.3) alloys before and after cycling (x=0: as-cast (a), after 30 cycles (b), after 80 cycles (c); x=0.3: as-cast (d), after 30 cycles (e), after 80 cycles (f)).

          Fig. 4 AES profiles of the La_0.7Mg_0.3Ni_2.65Mn_0.1Co_0.75 alloy electrodes before and after cycling (a) as cast; (b) after 10 cycles; (c) after 30 cycles.

             Fig. 5 AES profiles of the La_0.7Mg_0.3Ni_2.35Mn_0.1Co_0.75Al_0.3 alloy electrodes before and after cycling (a) as cast; (b) after 10 cycles; (c) after 30 cycles.  

Fig.4(a) and Fig.5(a), it is found that the oxygen content decreases drastically inside the alloy although it is high on the surface, which indicates that the high oxygen content on the alloy surface can be attributed to the adsorption of oxygen during exposure of the alloy in the air.It can be also found from Fig.5(b) that Mg content on the surfaces of the two alloys strongly increases after 10 cycles, which exhibits that Mg is firstly oxidized/ corroded for La-Mg-Ni-Co-based alloy electrodes, and subsequently forms a loose and permeable Mg(OH)₂ oxide layer on the alloy surface during the initial cycling stages. This oxide layer is very loose and a subsequent littleas protection to the alloy from being further corroded[15, 16], leading to the decrease of quantities of the active elements of Mg and La in the further cycling process and, consequently, a higherlowering the discharge capacity of degradation as shown in Fig. 1.

However, from Fig.5(c), it is seen that Al content on the alloy surface increases for the alloy with Al after 30 cycles. It can be concluded that Al is also oxidized/corroded and gradually formed an Al oxide film sduring cycling, and such an oxide film was very dense and protective[17]. Once Al oxide film forms on the alloy surface, further oxidation of the active components inhibited, and the anti-oxidation/corrosion capability of the alloy is increased. The formation of the Al oxide film is concluded to be the most factor of the improvement of the cycling stability of the alloy with Al during electrochemical cycling.

4  Conclusions

The improvement of the cycling stability of the La-Mg-Ni-based alloy electrodes by the partial substitution of Al for Ni can be attributed to two factors, one is the decrease of the pulverization of the alloy particles, the other is the increase of the anti-oxidation/corrosion of the alloy due to the formation of a a dense Al oxide film during cycling. After Ni is partially substituted by Al, the cell volume expansion ratio, ΔV/V, of the alloy upon hydrogenation decreases and the alloy particles pulverization is inhibited. The dense Al oxide film prevents further oxidation of the active components in the alloy, whichis concluded to be the most important reason for the improvement of cycling stability of the La_0.7Mg_0.3Ni_2.35Co_0.75Al_0.3 alloy electrode.

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Foundation item: Project (50131040) supported by the National Natural Science Foundation of China
Corresponding author: PAN Hong-ge; Tel: +86-571-87952576; Fax: +86-571-87951152; E-mail: honggepan@zjuem.zju.edu.cn

(Edited by LONG Huai-zhong)