# Effects of Magnesium Content on Structure and Electrochemical Properties of La-Mg-Pr-Al-Mn-Co-Ni Hydrogen Storage Alloys

Authors: L. M. C. Zarpelon; E. P. Banczek; L. G. Martinez; N. B. Lima; I. Costa; R. N. Faria
Journal: Advances in Materials Science and Engineering
 (2018)

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## Abstract

The discharge capacity, microstructures, and corrosion resistance of some as-cast alloys represented by the formula La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8, where x = 0.0, 0.1, 0.3, 0.5, and 0.7, were investigated by SEM/EDX, XRD, and electrochemical measurements. The partial substitution of La by Mg refined the grain structure while the total substitution changed it from equiaxed to columnar. Three phases were detected: a major phase (M), a grey phase (G), and a dark phase (D). The compositions analyzed by EDX suggested that the M phase was close to a LaNi5 phase. With the increase of the Mg content, the analyses revealed a G phase with composition close to a RMg2Ni9 (R = La,Pr) and a D phase close to a MgNi2 phase. The XRD analysis and Rietveld refinement corroborated the EDX results. The corrosion resistance of the alloys was evaluated in 6.0 mol·L−1 KOH solution, and the results showed that the substitution of La by Mg was beneficial for this alloy property. Nevertheless, Mg addition was deleterious to the discharge capacity of the electrodes.


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## Body

## 1. Introduction

Over the past years, extensive research has been concentrated on the study of hydrogen storage alloys as a negative electrode of nickel-metal hydride (Ni/MH) secondary battery, as shown in recent reviews on the subject [1–5]. Commercial alloy systems for Ni/MH batteries are rare earth-based AB5-type alloys, Ti- and Zr-based AB2-type alloys, and, recently, A2B7- and AB3-type RE-Mg-Ni-based superlattice alloys. Although representing the first generation of negative electrodes, the rare earth-based AB5-type alloys (with discharge capacity limited to 320 mAh/g) are very popular in use on commercial Ni/MH batteries [1]. Nickel substitution in La-Ni-type electrodes of AB5 system multicomponent metal hydride alloys has been widely reported, and the purpose of alloy modification is to improve the electrode performance. Aluminum, manganese, and/or cobalt are always present in Ni/MH electrodes. Lanthanum is frequently substituted for cerium, neodymium, and/or praseodymium. Magnesium has also been included in this type of hydrogen storage alloys as an element that can increase the number of hydrogen atoms stored per metal atom [6]. Mg additions vary from impurity levels to considerable atomic concentrations aiming to reduce costs (by reducing the amount of Co) and improving cyclic stability or durability of the Ni/MH batteries [7–11].Reported microstructural investigations and chemical analyses for as-cast hydrogen storage alloys with Mg addition are very scarce. This paper addresses this aspect and reports the results of a study with partial and total substitution of La by Mg, on hydrogen storage La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 as-cast alloys (x = 0.0, 0.1, 0.3, 0.5 and 0.7). A thorough investigation of the microstructures of these alloys and the phases present has been carried out using SEM/EDX and XRD. Moreover, it is well known that the Ni/MH batteries work in a strong oxidizing medium composed of high-concentration alkaline electrolyte. Therefore, among the desired properties of negative electrodes alloys, high corrosion resistance is essential for long cycle lifetime [6–13]. In the present study, the corrosion resistance of the La-Mg-Pr-Al-Mn-Co-Ni alloys in 6.0 mol·L−1·KOH solution was also investigated.


## 2. Experimental Procedures

The alloys investigated in this study were commercially prepared in 5 kg batches melted in induction heating vacuum equipment and cast in a cooled mold. The chemical analyses of the as-cast alloys are given in Table1. For comparison convenience, a conversion to the substitution composition (atomic %) is also provided.Table 1
Composition of the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
Nominal composition
x
Specified composition (at.%)
La
Pr
Mg
Al
Mn
Co
Ni
La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8
0.0
11.67
5.00
—
5.00
6.67
8.33
63.33
La0.6Mg0.1Pr0.3Al0.3Mn0.4Co0.5Ni3.8
0.1
10.00
5.00
1.67
5.00
6.67
8.33
63.33
La0.4Mg0.3Pr0.3Al0.3Mn0.4Co0.5Ni3.8
0.3
6.67
5.00
5.00
5.00
6.67
8.33
63.33
La0.2Mg0.5Pr0.3Al0.3Mn0.4Co0.5Ni3.8
0.5
3.34
5.00
8.33
5.00
6.67
8.33
63.33
Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8
0.7
—
5.00
11.67
5.00
6.67
8.33
63.33Agreement has been found between the composition specified values and that determined by analyses in the alloys. As per the supplier’s analysis, the alloys contained sulfur, oxygen, carbon, and nitrogen as impurities (≤100 ppm). Specimens for microstructure investigations were prepared using standard metallographic methods. The microstructures of the samples were examined using a scanning electron microscopy (SEM) with energy dispersive X-ray (EDX) analysis facility (Philips XL30). Average data were obtained from various independent measurements from each phase. The crystal structure of the alloys was identified by X-ray diffraction (XRD) with a Cu Kα radiation (Rigaku DMAX-2000). The phase abundance, lattice parameters, and cell volume of the alloy phases were obtained from Rietveld refinement method using GSAS (General Structure Analysis System) program.The corrosion studies of the alloys was evaluated by electrochemical methods, specifically electrochemical impedance spectroscopy (EIS) and potentiodynamic polarization curves (anodic and cathodic, separately). Electrochemical measurements have been used in previous papers [14, 15]. A three-electrode cell was employed in this investigation with a Pt counter electrode and a mercurous oxide (Hg/HgO/6.0 mol·L−1·KOH solution) as a standard reference electrode. The working electrode was produced using cold epoxy resin mounting with a contact wire for electric connection. The surface for exposure to the electrolyte was polished prior testing. The corrosion behavior was investigated with a Gamry frequency response analyzer (EIS 300) linked to a potentiostat (PCI4/300). The corrosion tests were performed in a 6.0 mol·L−1·KOH solution at room temperature (20 ± 2)°C. All the reagents employed for the test solution were per analytical (p.a.) grade.The specimens were immersed in the test solution, and the open circuit potential (OCP) was determined as a function of time. EIS tests were performed employing perturbation voltage amplitude of ±10 mV, relatively to the OCP, from 10 kHz to 10 mHz, with an acquisition rate of 10 points/decade. Soon after the EIS tests, the OCP was measured to test the stability of the potential. Potentiodynamic polarization curves were obtained employing a scan rate of 30 mV/s. Polarization curves with slower scan rates were unsuccessful due to the highly passive character of the alloys in the electrolyte employed (resulting only in scattered data). Four specimens of each commercial alloy were examined in this investigation.Discharge capacity test electrodes were produced by pressing a mixture of 100 mg of the commercial alloy (powdered by manual crushing to a 270 mesh sieve) and teflonized carbon (Vulcan XC-72R with 33 wt.% polytetrafluoroethylene) in a weight ratio of 1 : 1 on both sides of a nickel mesh (10 mm diameter). The charge/discharge cycling tests were carried out at 25°C employing a commercial battery analyzer (Arbin BT-4). Discharge capacity assessments were performed in a trielectrode cell consisting of the prepared working electrode, a coiled Pt wire (0.5 mm in diameter and 300 mm long) counter electrode, and a Hg/HgO/6.0 mol·L−1·KOH solution reference electrode in a 6.0 mol·L−1·KOH electrolyte solution. The working electrode was charged at 100 mA/g for 5 h and subsequently discharged at 50 mA/g to the cutoff potential of −0.6 V versus the Hg/HgO reference electrode.


## 3. Results and Discussion

### 3.1. SEM and EDX Characterization

Backscattered electron micrographs showing a general view and details of the as-cast alloys are shown in Figures1 and 2, respectively. The La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 alloy (Figure 2(a)) is composed of a major phase (M) and a grey phase (G) in the grain boundaries. The other alloys are composed of three phases: M, G, and a dark phase (D). The proportion of these three phases in the alloys changed as Mg was included and also as its content increased. Total substitution of La by Mg (x = 0.7) makes the M phase the minor phase in the Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 alloy (Figure 2(e)). In this case, the M phase is inside the grey phase. The morphologies of the as-cast alloys also reveal that substitution of lanthanum by magnesium results in a marked refinement in the grain structure of the alloys (Figure 1). Clearly, the magnesium-free alloy shows a coarse equiaxed grain structure, whereas the lanthanum-free alloy reveals a fine structure with columnar grain. Previous study has shown that the total substitution of lanthanum by praseodymium in the alloy changed the grain structure from equiaxed to columnar [16]. This result and the present observation indicate that the presence of lanthanum in the alloys favors an equiaxed grain structure.Figure 1
SEM micrographs showing a general view of the alloys investigated: (a) La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (b) La0.6Mg0.1Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (c) La0.4Mg0.3Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (d) La0.2Mg0.5Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (e) Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8.Figure 2
SEM micrographs showing theM, G, and D phases of the alloys investigated: (a) La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (b) La0.6Mg0.1Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (c) La0.4Mg0.3Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (d) La0.2Mg0.5Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (e) Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8.The chemical composition of the major phase in the different alloys, as determined by EDX, is presented in Table2. The M phase in the Mg-free alloy revealed a (La,Pr) : (Al,Mn,Co,Ni) atomic ratio of 5.0, indicating it to be a 1 : 5 phase (similar to LaNi5). This result would be in agreement with the LaNi5 matrix phase observed in previous studies [17–20]. The subsequent alloys (x > 0.0) showed that this (La,Pr) : (Al,Mn,Co,Ni) atomic ratio increases due to the substitution of La by Mg. Despite the increase of the praseodymium content, the total rare earth content in the M phase decreased from 16.7 at.% to 14.0 at.% with the total substitution of La by Mg. Conversely, the nickel content in the M phase of these alloys increased from 63.4 at.% to 72.0 at.% with this substitution. The amount of aluminum and manganese in this phase decreased somewhat with increasing magnesium content in the alloys. The cobalt content showed an average close to 8 at.%.Table 2
Composition determined using EDX at the centers of theM phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.0 (5)
12.0 ± 0.2
4.7 ± 0.4
—
5.5 ± 0.5
5.8 ± 1.4
8.6 ± 0.2
63.4 ± 1.3
5.0
0.1 (2)
11.0 ± 0.5
5.3 ± 0.1
—
3.6 ± 1.1
3.1 ± 1.1
7.7 ± 0.2
69.4 ± 2.3
5.1
0.3 (11)
8.5 ± 0.1
7.0 ± 0.4
—
4.2 ± 0.6
3.1 ± 0.9
8.2 ± 0.4
68.0 ± 1.5
5.4
0.5 (11)
5.9 ± 0.2
9.7 ± 0.3
—
3.6 ± 0.4
3.1 ± 0.5
8.0 ± 0.4
70.0 ± 0.7
5.4
0.7 (5)
—
14.0 ± 0.2
—
3.4 ± 0.4
2.8 ± 0.3
7.6 ± 0.3
72.0 ± 0.8
6.1
∗Number of independent measurements from the M phase. ∗∗(La,Pr)/(Al,Mn,Co,Ni).The chemical composition of the grey phase observed in all alloys, also determined using EDX, is shown in Table3. As in the previous case, in all alloys the La content showed a decrease, whereas the Pr content increases in this phase. The measured value of the rare earth (9.1∼10.4 at.%) was more than half of that found in the M phase (14.0∼16.7 at.%). The magnesium content in this grey phase was as high as 12.5 at.%, which indicates the preferential concentration of this element in this phase. Similar to that observed in the matrix phase, the amount of Al and Mn in the grey phase diminished with the substitution of La by Mg. The aluminum content in the G phase (1.7∼4.0 at.%) was somewhat lower than that found in the M phase (3.4∼5.5 at.%). It was also detected a manganese concentration peak in the Mg-free alloy (∼22 at.%), which indicated the presence of a possible phase rich in Mn, in a very reduced amount, as observed in the correspondent micrograph (Figure 2(a)). The presence of this phase can be attributed to the as-cast state of the alloys. On the other hand, in the alloys with x > 0.0, the grey phase revealed a (La,Pr) : Mg : (Al,Mn,Co,Ni) atomic ratio close to 1 : 2 : 9. This ratio would indicate the presence of phase similar to the RMg2Ni9 type, in agreement with the system AB2C9 [21, 22]. The average cobalt content (∼7 at.%) was close to that in the M phase (∼8 at.%).Table 3
Composition determined using EDX at the centers of theG phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.0 (8)
8.1 ± 0.4
2.3 ± 0.4
—
4.0 ± 0.3
21.8 ± 1.4
8.5 ± 0.8
55.3 ± 1.3
—
0.1 (4)
6.4 ± 0.3
2.9 ± 0.2
10.9 ± 0.4
2.9 ± 0.2
10.3 ± 0.4
7.9 ± 0.3
58.7 ± 0.5
1 : 2.3 : 7.5
0.3 (7)
5.0 ± 0.3
4.3 ± 0.2
12.0 ± 0.6
3.7 ± 0.1
6.5 ± 0.5
7.4 ± 0.2
61.0 ± 0.3
1 : 2.0 : 8.0
0.5 (2)
3.5 ± 0.2
5.9 ± 0.3
12.4 ± 0.4
2.8 ± 0.1
4.8 ± 0.5
6.8 ± 0.6
63.8 ± 0.2
1 : 1.8 : 7.8
0.7 (6)
—
9.1 ± 0.3
12.5 ± 0.5
1.7 ± 0.2
3.8 ± 0.3
5.8 ± 0.5
67.0 ± 0.7
1 : 1.8 : 8.2
∗Number of independent measurements from the G phase. ∗∗(La,Pr)/(Mg)/(Al,Mn,Co,Ni).The chemical composition of the dark phase in the different alloys is presented in Table4. This phase has not been found in the Mg-free alloy. Apparently, magnesium influences the microstructure and also the phases that can be found in the alloys. In this phase, the rare earth content was close or below the EDX detection limit, indicating the preferential concentration of these elements in the other detected phases. For x = 0.1, the dark phase was richer in manganese and aluminum in contrast to the other constituents (except Ni). Only in the La-free alloy (x = 0.7) was observed a magnesium concentration peak. The approximated atomic relation between Mg and Ni in this alloy suggests the presence of similar phase to the MgNi2 phase. This observation would be in agreement upon observations in the synthesis of ternary RMg2Ni9 alloys by sintering of powders of MgNi2 and RNi5 (R = La, Ce, Pr, Nd, Sm, and Gd) [22]. Except for x = 0.7, the values measured showed a preferential presence of aluminum in the D phase in comparison with the concentrations found in the M and G phases. In the case of manganese, after the peak of concentration in x = 0.1, it was observed a decrease in the other compositions. For the cobalt content, some variations with higher values of x = 0.3 and 0.5 were observed. It must be kept in mind that the characterization of the alloys was carried out in the as-cast state, and deviation in the results can be attributed to the alloys’ heterogeneous condition. This is consistent with previous studies [18, 23], where it was shown that, in a La0.7Mg0.3Al0.2Mn0.1Co0.75Ni2.45 alloy, annealing at high temperature was essential to achieve a homogeneous composition. EDX determinations indicate phase compositions close to LaNi5 in the phase matrix, RMg2Ni9 (R = La, Pr) in the grey phase, and MgNi2 in the dark phase.Table 4
Composition determined using EDX at the centers of theD phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.1 (4)
<1
<1
<1
16–17
23–24
7–8
49–50
1.4
0.3 (6)
<1
<1
1–8
10–17
15–16
15–16
56–57
2.8
0.5 (8)
<1
<1
1–18
3–11
12–13
15–16
60–63
3.1
0.7 (5)
—
<1
21–23
1–2
7–9
5–13
61–65
2.0
∗Number of independent measurements from the D phase. ∗∗(Pr,Mg,Al,Mn)/(Co,Ni).


### 3.2. XRD Characterization

The XRD profiles of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0, 0.1, 0.3, 0.5, 0.7) as-cast alloys are shown in Figure 3. It can be observed that the diffraction peaks were shifted to higher angles due to the La substitution (atomic radius 2.74 Ǻ) by Mg (atomic radius 1.72 Ǻ), also noting the constant presence of Pr (atomic radius 2.67 Ǻ) in all compositions. The identification of phases by XRD was based on the results obtained by SEM/EDX. The identified phases, the lattice parameters, unit cell volumes, and Rietveld phase abundance are listed in Table 5 and are also shown in Figures 4 and 5. The substitution led to a decrease in the lattice parameters and unit cells of the phases present in the alloys. There have been identified phases with similar crystalline symmetry and spatial group as reference phases LaNi5, PrNi5, LaMg2Ni9, PrMg2Ni9, AlMnNi6, and MgNi2. However, for the a and c parameters, there have been observed variations when compared to these reference phases. There have been attributed to possible substitutions in the crystalline lattice in the sites of La (La,Pr) and of Ni (Al,Mn,Co,Ni) as a consequence of the as-cast state of the alloys. Both, this condition and the increased substitution of La by Mg, influenced the phase’s relative abundance, as shown in Figure 5. Also shown in this figure are the correspondence with the matrix phase (M), grey phase (G), and dark phase (D), all determined by SEM/EDX analyses for the Mg alloys.Figure 3
XRD profiles of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.Table 5
The characteristics of alloy phases in the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x=0.0–0.7) alloys.
Samples
Phases
Space group
Parameters of fita
Phase abundance (wt.%)
Lattice parameter (Ǻ)
Cell volume (Ǻ3)
a
c
x=0.0
LaNi5
P6/mmm
R
p
=0.2660
74.2
5.047
4.063
89.6 ± 0.5
PrNi5
P6/mmm
R
wp
=0.4664, χ2 = 2.757
25.8
5.034
4.034
88.5 ± 0.5
x = 0.1
LaNi5
P6/mmm
R
p
=0.2416
43.0
5.017
4.062
88.5 ± 0.5
PrNi5
P6/mmm
R
wp
=0.4440, χ2= 2.467
45.5
5.020
4.019
87.7 ± 0.5
(La,Pr)Mg2Ni9
R-3m
11.5
4.950
24.299
516 ± 1
x = 0.3
(La,Pr)Ni5
P6/mmm
R
p
=0.2416
60.7
4.996
4.051
87.6 ± 0.5
(La,Pr)Mg2Ni9
R-3m
R
wp
=0.4440, χ2 = 2.467
29.3
4.936
24.104
509 ± 1
AlMnNi6
Pm3m
10.0
3.603
3.603
46.8 ± 0.5
x = 0.5
(La,Pr)Ni5
P6/mmm
R
p
=0.2469
32.6
4.981
4.041
86.8 ± 0.5
(La,Pr)Mg2Ni9
R-3m
R
wp
=0.6088, χ2 = 2.148
42.6
4.932
23.993
505 ± 1
AlMnNi6
Pm3m
24.8
3.590
3.590
46.3 ± 0.5
x = 0.7
PrNi5
P6/mmm
R
p
=0.2056
5.8
4.943
4.028
85.2 ± 0.5
PrMg2Ni9
R-3m
R
wp
= 0.3734, χ2 = 2.249
46.4
4.918
23.906
501 ± 1
AlMnNi6
Pm3m
33.5
3.583
3.583
46.0 ± 0.5
MgNi2
P63/mmc
14.3
4.834
15.824
320 ± 1
a
R
p = pattern factor; Rwp = weighted pattern factor; χ2 = goodness of fit.Figure 4
The lattice parameters and cell volumes of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x=0.0–0.7) alloys: (a) LaNi5, PrNi5, and (La,Pr)Ni5 phases; (b) (La,Pr)Mg2Ni9 and PrMg2Ni9 phases.
(a)
(b)Figure 5
The phase abundance of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.The phase abundance of the phase similar to LaNi5 for x = 0.0 and 0.1 diminished from 74.2% to 43.0%, whereas for the phase similar to PrNi5 increased from 25.8% to 45.5%. It was also detected for x = 0.1 a phase similar to (La,Pr)Mg2Ni9 (11.5%). The abundance of this phase showed a steady increase with the amount of Mg in the alloy (x = 0.1 to 0.5) and the detection of a PrMg2Ni9-type phase on the total substitution of La by Mg (Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8).(La,Pr)Ni5 shifted from major abundance (60.7%) for x = 0.3 to minor abundance (5.8%) for x = 0.7. It has also been identified from x = 0.3 a phase similar to the AlMnNi6 phase in increasing abundance that reached 33.5% for x = 0.7. In this condition, that is, total substitution of La by Mg, it has been detected a phase similar to the MgNi2 phase (14.3%). The identification of phases present in the alloys by XRD and SEM/EDX led to the following correspondences: M to LaNi5 and PrNi5-type phases, G to LaMg2Ni9 and PrMg2Ni9-type phases, and D to MgNi2 and AlMnNi6-type phases.


### 3.3. Electrochemical Characterization

#### 3.3.1. Corrosion

Figure6 shows the anodic potentiodynamic polarization curves for the various tested alloys. At the corrosion potential, most alloys presented very low current densities (i), in the order of 10−5 to 10−6 A/cm2, typical of passive materials, but the lowest i value was related to the alloy with the highest Mg-content (x = 0.7). For the alloy without Mg (x = 0), the current density largely increased with overpotential showing that the passive film on this alloy had the lowest resistance. The passive films on the alloys with 0.6 and 0.4 at.% La content showed intermediate resistances, between that without Mg and that without La. These results show that electrochemical behavior of the alloys was highly dependent on their microstructures. The substitution of La by Mg that led to refinement in the grain structure also had a beneficial effect on their corrosion resistance.Figure 6
Anodic polarization curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys in 6.0 mol·L−1·KOH solution.The polarization curves show that from the corrosion potential up to 0.7 V the effect of the alloy composition and consequently its microstructure on the electrochemical behavior is clearly seen with the lowest current densities associated with the alloys with lower La contents, that is, increasing Mg concentration. At potentials of nearly 0.7 V, all alloys showed a current density increase, and from 0.8 V upwards the electrochemical behavior of the alloys with Mg-contents of 0.0, 0.1, 0.3, and 0.5 at.% was similar. On the other hand, for the alloy with total substitution of La by Mg, the current density values were lower than the other alloys in the whole potential range.The Nyquist diagrams for the various alloys studied are shown in Figure7. The EIS results showed higher impedances associated with the samples with the higher Mg-contents (x = 0.5 and x = 0.7), indicating a passive behavior for these alloys. The lowest impedances were associated with the alloy without Mg and supported the polarization results that indicated that this alloy presented the lowest corrosion resistance.Figure 7
Nyquist diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.The Bode phase angle diagrams in Figure8 show two time constants for all studied alloys with lower phase angles related to the alloys with low Mg contents (0.0, 0.1, and 0.3 at.%). For the alloys with 0.5 or 0.7 at.% Mg (without La), the time constant at high frequencies is seen at approximately 1 kHz, whereas for the other alloys, this time constant occurs at nearly 0.1 kHz. For all alloys, the second time constant is seen at approximately the same frequency, 0.1 Hz. The high frequency time constant is related to the surface oxide/hydroxide film, whereas the one at lower frequencies is associated with charge transfer processes. These results indicate that more protective surface films are formed on the alloys with the high Mg contents. This is most likely related to the refined grain microstructure associated with these alloys and shows that the substitution of La by Mg increases the alloy corrosion resistance mainly due to the formation of a more protective oxide film on their surface comparatively to that formed on the alloys with larger La contents. Passive surface films such as La(OH)3 and Mg(OH)2 have been reported in literature for La-Mg-Ni ternary alloy systems [24, 25]. Due to the very low reduction potentials associated with Mg and rare earth elements, such as La and Pr, in alkaline environments, these types of passive films are fairly stable [26].Figure 8
Bode phase angle diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5 and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.


#### 3.3.2. Discharge Capacity

Figure9 shows the discharge capacity characteristics of the alloy electrodes with cycling. The range of measured discharge capacity values, limited to 250 mAh/g, could be attributed to superficial oxide formation during the preparation of the electrodes in the air. It can be seen that the electrodes can be easily activated within 2 cycles. Higher discharge capacity values were obtained for the Mg-free alloy with a maximum of 250 mAh/g and for x = 0.1 (maximum of 220 mAh/g). A significant decrease was observed for x = 0.3 (maximum ∼140 mAh/g), and a dramatic reduction in this property with higher amount of Mg was observed. Clearly, increasing the magnesium content on the alloys decreased the discharge capacity of the negative electrodes. From the structural viewpoint, the increasing amount of Mg decreased the presence of the phase similar to the LaNi5-type phase in the alloys, and the consequent increase of the abundance of the others observed phases (phases similar to the (La,Pr)Mg2Ni9 and MgNi2 phases). Notwithstanding the limitation of the discharge capacity showed experimentally by the LaNi5 phase (hexagonal, type CaCu5) [5, 27], the performance of this phase still overcame the (La,Pr)Mg2Ni9 and MgNi2 phases. The (La,Pr)Mg2Ni9 phases follow the structural model formed by the relation between the subunities (MgNi2)/(LaNi5) equal to 2. The subunity MgNi2 present (Laves phases, hexagonal type MgNi2) shows some slow performance for hydrogen storage very similar to that individually presented by the MgNi2 alloy (H/M∼0.33% in mass) [21]. Conversely, the hydride corresponding to the LaNi5 phase shows a hydrogen storage capacity H/M of 1.4% in mass [28]. Thus, comparatively, the higher abundance of the phase similar to the LaNi5 phase demonstrated to be beneficial to a higher discharge capacity of the electrodes. Furthermore, the refining of the alloys’ microstructure that followed the increasing substitution of La by Mg showed unfavorable to the discharge capacity. Counteracting this effect, the refining proved to be beneficial to the corrosion resistance, as indicated by the experimental results. Thus, magnesium addition proved to be favorable to the corrosion properties, but high amounts have shown to be deleterious to the discharge capacity of the alloy electrodes tested. The overall discharge capacities of the present as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys were somewhat superior to those obtained using mechanical alloying with a composition of La1−xMgxAl0.4Mn0.3Co0.3Ni3.8 (x = 0–0.2) [7]. On the other hand, better discharge capacities were obtained with La-rich mischmetal (MI) electrodes of MI1−xMgxAl0.10Mn0.10Co0.55Ni3.0 (x = 0.05–0.30) alloys [8]. These discrepancies can be attributed to the alloy preparation method, to testing conditions, and to the slight differences in the alloys compositions.Figure 9
Discharge capacity of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys versus cycle number.Figure10 shows the discharge potential curves of the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys. It is well known that the principle of operation of a Ni/MH battery is based on the ability of certain metals, alloys, or intermetallics to absorb hydrogen in a reversible way. The hydride formation/decomposition process occurs via electrochemical charge transfer reaction [5, 29]. It can be seen in Figure 10 that for the first three conditions of substitution of La by Mg (x = 0.0, x = 0.1, and x = 0.3) it is possible to identify two regions that are commonly present in the curves of discharge potentials. The relatively flat part is called potential plateau and corresponds to the discharge process controlled by charge transfer. On the other hand, the final part of the curve represents the striking decrease of the potential due to the depletion of hydrogen atoms from the electrode surface. Additionally, the discharge potential also decreases with the increase of the internal resistance of the alloy. The internal resistance of alloy generally includes contact resistance, charge transfer resistance, and diffusion resistance [30]. The La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0) electrode alloy presented the longest potential plateau, indicating more effective charge transfer process and lower internal resistance compared to the other studied alloys. Again, the substitution of La by Mg in the alloys studied, considering the structural changes that resulted, proved to be deleterious to the discharge capacity of the electrodes.Figure 10
The discharge potential curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.


## 3.1. SEM and EDX Characterization

Backscattered electron micrographs showing a general view and details of the as-cast alloys are shown in Figures1 and 2, respectively. The La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 alloy (Figure 2(a)) is composed of a major phase (M) and a grey phase (G) in the grain boundaries. The other alloys are composed of three phases: M, G, and a dark phase (D). The proportion of these three phases in the alloys changed as Mg was included and also as its content increased. Total substitution of La by Mg (x = 0.7) makes the M phase the minor phase in the Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 alloy (Figure 2(e)). In this case, the M phase is inside the grey phase. The morphologies of the as-cast alloys also reveal that substitution of lanthanum by magnesium results in a marked refinement in the grain structure of the alloys (Figure 1). Clearly, the magnesium-free alloy shows a coarse equiaxed grain structure, whereas the lanthanum-free alloy reveals a fine structure with columnar grain. Previous study has shown that the total substitution of lanthanum by praseodymium in the alloy changed the grain structure from equiaxed to columnar [16]. This result and the present observation indicate that the presence of lanthanum in the alloys favors an equiaxed grain structure.Figure 1
SEM micrographs showing a general view of the alloys investigated: (a) La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (b) La0.6Mg0.1Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (c) La0.4Mg0.3Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (d) La0.2Mg0.5Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (e) Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8.Figure 2
SEM micrographs showing theM, G, and D phases of the alloys investigated: (a) La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (b) La0.6Mg0.1Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (c) La0.4Mg0.3Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (d) La0.2Mg0.5Pr0.3Al0.3Mn0.4Co0.5Ni3.8; (e) Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8.The chemical composition of the major phase in the different alloys, as determined by EDX, is presented in Table2. The M phase in the Mg-free alloy revealed a (La,Pr) : (Al,Mn,Co,Ni) atomic ratio of 5.0, indicating it to be a 1 : 5 phase (similar to LaNi5). This result would be in agreement with the LaNi5 matrix phase observed in previous studies [17–20]. The subsequent alloys (x > 0.0) showed that this (La,Pr) : (Al,Mn,Co,Ni) atomic ratio increases due to the substitution of La by Mg. Despite the increase of the praseodymium content, the total rare earth content in the M phase decreased from 16.7 at.% to 14.0 at.% with the total substitution of La by Mg. Conversely, the nickel content in the M phase of these alloys increased from 63.4 at.% to 72.0 at.% with this substitution. The amount of aluminum and manganese in this phase decreased somewhat with increasing magnesium content in the alloys. The cobalt content showed an average close to 8 at.%.Table 2
Composition determined using EDX at the centers of theM phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.0 (5)
12.0 ± 0.2
4.7 ± 0.4
—
5.5 ± 0.5
5.8 ± 1.4
8.6 ± 0.2
63.4 ± 1.3
5.0
0.1 (2)
11.0 ± 0.5
5.3 ± 0.1
—
3.6 ± 1.1
3.1 ± 1.1
7.7 ± 0.2
69.4 ± 2.3
5.1
0.3 (11)
8.5 ± 0.1
7.0 ± 0.4
—
4.2 ± 0.6
3.1 ± 0.9
8.2 ± 0.4
68.0 ± 1.5
5.4
0.5 (11)
5.9 ± 0.2
9.7 ± 0.3
—
3.6 ± 0.4
3.1 ± 0.5
8.0 ± 0.4
70.0 ± 0.7
5.4
0.7 (5)
—
14.0 ± 0.2
—
3.4 ± 0.4
2.8 ± 0.3
7.6 ± 0.3
72.0 ± 0.8
6.1
∗Number of independent measurements from the M phase. ∗∗(La,Pr)/(Al,Mn,Co,Ni).The chemical composition of the grey phase observed in all alloys, also determined using EDX, is shown in Table3. As in the previous case, in all alloys the La content showed a decrease, whereas the Pr content increases in this phase. The measured value of the rare earth (9.1∼10.4 at.%) was more than half of that found in the M phase (14.0∼16.7 at.%). The magnesium content in this grey phase was as high as 12.5 at.%, which indicates the preferential concentration of this element in this phase. Similar to that observed in the matrix phase, the amount of Al and Mn in the grey phase diminished with the substitution of La by Mg. The aluminum content in the G phase (1.7∼4.0 at.%) was somewhat lower than that found in the M phase (3.4∼5.5 at.%). It was also detected a manganese concentration peak in the Mg-free alloy (∼22 at.%), which indicated the presence of a possible phase rich in Mn, in a very reduced amount, as observed in the correspondent micrograph (Figure 2(a)). The presence of this phase can be attributed to the as-cast state of the alloys. On the other hand, in the alloys with x > 0.0, the grey phase revealed a (La,Pr) : Mg : (Al,Mn,Co,Ni) atomic ratio close to 1 : 2 : 9. This ratio would indicate the presence of phase similar to the RMg2Ni9 type, in agreement with the system AB2C9 [21, 22]. The average cobalt content (∼7 at.%) was close to that in the M phase (∼8 at.%).Table 3
Composition determined using EDX at the centers of theG phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.0 (8)
8.1 ± 0.4
2.3 ± 0.4
—
4.0 ± 0.3
21.8 ± 1.4
8.5 ± 0.8
55.3 ± 1.3
—
0.1 (4)
6.4 ± 0.3
2.9 ± 0.2
10.9 ± 0.4
2.9 ± 0.2
10.3 ± 0.4
7.9 ± 0.3
58.7 ± 0.5
1 : 2.3 : 7.5
0.3 (7)
5.0 ± 0.3
4.3 ± 0.2
12.0 ± 0.6
3.7 ± 0.1
6.5 ± 0.5
7.4 ± 0.2
61.0 ± 0.3
1 : 2.0 : 8.0
0.5 (2)
3.5 ± 0.2
5.9 ± 0.3
12.4 ± 0.4
2.8 ± 0.1
4.8 ± 0.5
6.8 ± 0.6
63.8 ± 0.2
1 : 1.8 : 7.8
0.7 (6)
—
9.1 ± 0.3
12.5 ± 0.5
1.7 ± 0.2
3.8 ± 0.3
5.8 ± 0.5
67.0 ± 0.7
1 : 1.8 : 8.2
∗Number of independent measurements from the G phase. ∗∗(La,Pr)/(Mg)/(Al,Mn,Co,Ni).The chemical composition of the dark phase in the different alloys is presented in Table4. This phase has not been found in the Mg-free alloy. Apparently, magnesium influences the microstructure and also the phases that can be found in the alloys. In this phase, the rare earth content was close or below the EDX detection limit, indicating the preferential concentration of these elements in the other detected phases. For x = 0.1, the dark phase was richer in manganese and aluminum in contrast to the other constituents (except Ni). Only in the La-free alloy (x = 0.7) was observed a magnesium concentration peak. The approximated atomic relation between Mg and Ni in this alloy suggests the presence of similar phase to the MgNi2 phase. This observation would be in agreement upon observations in the synthesis of ternary RMg2Ni9 alloys by sintering of powders of MgNi2 and RNi5 (R = La, Ce, Pr, Nd, Sm, and Gd) [22]. Except for x = 0.7, the values measured showed a preferential presence of aluminum in the D phase in comparison with the concentrations found in the M and G phases. In the case of manganese, after the peak of concentration in x = 0.1, it was observed a decrease in the other compositions. For the cobalt content, some variations with higher values of x = 0.3 and 0.5 were observed. It must be kept in mind that the characterization of the alloys was carried out in the as-cast state, and deviation in the results can be attributed to the alloys’ heterogeneous condition. This is consistent with previous studies [18, 23], where it was shown that, in a La0.7Mg0.3Al0.2Mn0.1Co0.75Ni2.45 alloy, annealing at high temperature was essential to achieve a homogeneous composition. EDX determinations indicate phase compositions close to LaNi5 in the phase matrix, RMg2Ni9 (R = La, Pr) in the grey phase, and MgNi2 in the dark phase.Table 4
Composition determined using EDX at the centers of theD phase in the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys.
x (N∗)
Analyzed composition (at.%)
Ratio∗∗
La
Pr
Mg
Al
Mn
Co
Ni
0.1 (4)
<1
<1
<1
16–17
23–24
7–8
49–50
1.4
0.3 (6)
<1
<1
1–8
10–17
15–16
15–16
56–57
2.8
0.5 (8)
<1
<1
1–18
3–11
12–13
15–16
60–63
3.1
0.7 (5)
—
<1
21–23
1–2
7–9
5–13
61–65
2.0
∗Number of independent measurements from the D phase. ∗∗(Pr,Mg,Al,Mn)/(Co,Ni).


## 3.2. XRD Characterization

The XRD profiles of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0, 0.1, 0.3, 0.5, 0.7) as-cast alloys are shown in Figure 3. It can be observed that the diffraction peaks were shifted to higher angles due to the La substitution (atomic radius 2.74 Ǻ) by Mg (atomic radius 1.72 Ǻ), also noting the constant presence of Pr (atomic radius 2.67 Ǻ) in all compositions. The identification of phases by XRD was based on the results obtained by SEM/EDX. The identified phases, the lattice parameters, unit cell volumes, and Rietveld phase abundance are listed in Table 5 and are also shown in Figures 4 and 5. The substitution led to a decrease in the lattice parameters and unit cells of the phases present in the alloys. There have been identified phases with similar crystalline symmetry and spatial group as reference phases LaNi5, PrNi5, LaMg2Ni9, PrMg2Ni9, AlMnNi6, and MgNi2. However, for the a and c parameters, there have been observed variations when compared to these reference phases. There have been attributed to possible substitutions in the crystalline lattice in the sites of La (La,Pr) and of Ni (Al,Mn,Co,Ni) as a consequence of the as-cast state of the alloys. Both, this condition and the increased substitution of La by Mg, influenced the phase’s relative abundance, as shown in Figure 5. Also shown in this figure are the correspondence with the matrix phase (M), grey phase (G), and dark phase (D), all determined by SEM/EDX analyses for the Mg alloys.Figure 3
XRD profiles of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.Table 5
The characteristics of alloy phases in the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x=0.0–0.7) alloys.
Samples
Phases
Space group
Parameters of fita
Phase abundance (wt.%)
Lattice parameter (Ǻ)
Cell volume (Ǻ3)
a
c
x=0.0
LaNi5
P6/mmm
R
p
=0.2660
74.2
5.047
4.063
89.6 ± 0.5
PrNi5
P6/mmm
R
wp
=0.4664, χ2 = 2.757
25.8
5.034
4.034
88.5 ± 0.5
x = 0.1
LaNi5
P6/mmm
R
p
=0.2416
43.0
5.017
4.062
88.5 ± 0.5
PrNi5
P6/mmm
R
wp
=0.4440, χ2= 2.467
45.5
5.020
4.019
87.7 ± 0.5
(La,Pr)Mg2Ni9
R-3m
11.5
4.950
24.299
516 ± 1
x = 0.3
(La,Pr)Ni5
P6/mmm
R
p
=0.2416
60.7
4.996
4.051
87.6 ± 0.5
(La,Pr)Mg2Ni9
R-3m
R
wp
=0.4440, χ2 = 2.467
29.3
4.936
24.104
509 ± 1
AlMnNi6
Pm3m
10.0
3.603
3.603
46.8 ± 0.5
x = 0.5
(La,Pr)Ni5
P6/mmm
R
p
=0.2469
32.6
4.981
4.041
86.8 ± 0.5
(La,Pr)Mg2Ni9
R-3m
R
wp
=0.6088, χ2 = 2.148
42.6
4.932
23.993
505 ± 1
AlMnNi6
Pm3m
24.8
3.590
3.590
46.3 ± 0.5
x = 0.7
PrNi5
P6/mmm
R
p
=0.2056
5.8
4.943
4.028
85.2 ± 0.5
PrMg2Ni9
R-3m
R
wp
= 0.3734, χ2 = 2.249
46.4
4.918
23.906
501 ± 1
AlMnNi6
Pm3m
33.5
3.583
3.583
46.0 ± 0.5
MgNi2
P63/mmc
14.3
4.834
15.824
320 ± 1
a
R
p = pattern factor; Rwp = weighted pattern factor; χ2 = goodness of fit.Figure 4
The lattice parameters and cell volumes of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x=0.0–0.7) alloys: (a) LaNi5, PrNi5, and (La,Pr)Ni5 phases; (b) (La,Pr)Mg2Ni9 and PrMg2Ni9 phases.
(a)
(b)Figure 5
The phase abundance of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.The phase abundance of the phase similar to LaNi5 for x = 0.0 and 0.1 diminished from 74.2% to 43.0%, whereas for the phase similar to PrNi5 increased from 25.8% to 45.5%. It was also detected for x = 0.1 a phase similar to (La,Pr)Mg2Ni9 (11.5%). The abundance of this phase showed a steady increase with the amount of Mg in the alloy (x = 0.1 to 0.5) and the detection of a PrMg2Ni9-type phase on the total substitution of La by Mg (Mg0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8).(La,Pr)Ni5 shifted from major abundance (60.7%) for x = 0.3 to minor abundance (5.8%) for x = 0.7. It has also been identified from x = 0.3 a phase similar to the AlMnNi6 phase in increasing abundance that reached 33.5% for x = 0.7. In this condition, that is, total substitution of La by Mg, it has been detected a phase similar to the MgNi2 phase (14.3%). The identification of phases present in the alloys by XRD and SEM/EDX led to the following correspondences: M to LaNi5 and PrNi5-type phases, G to LaMg2Ni9 and PrMg2Ni9-type phases, and D to MgNi2 and AlMnNi6-type phases.


## 3.3. Electrochemical Characterization

### 3.3.1. Corrosion

Figure6 shows the anodic potentiodynamic polarization curves for the various tested alloys. At the corrosion potential, most alloys presented very low current densities (i), in the order of 10−5 to 10−6 A/cm2, typical of passive materials, but the lowest i value was related to the alloy with the highest Mg-content (x = 0.7). For the alloy without Mg (x = 0), the current density largely increased with overpotential showing that the passive film on this alloy had the lowest resistance. The passive films on the alloys with 0.6 and 0.4 at.% La content showed intermediate resistances, between that without Mg and that without La. These results show that electrochemical behavior of the alloys was highly dependent on their microstructures. The substitution of La by Mg that led to refinement in the grain structure also had a beneficial effect on their corrosion resistance.Figure 6
Anodic polarization curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys in 6.0 mol·L−1·KOH solution.The polarization curves show that from the corrosion potential up to 0.7 V the effect of the alloy composition and consequently its microstructure on the electrochemical behavior is clearly seen with the lowest current densities associated with the alloys with lower La contents, that is, increasing Mg concentration. At potentials of nearly 0.7 V, all alloys showed a current density increase, and from 0.8 V upwards the electrochemical behavior of the alloys with Mg-contents of 0.0, 0.1, 0.3, and 0.5 at.% was similar. On the other hand, for the alloy with total substitution of La by Mg, the current density values were lower than the other alloys in the whole potential range.The Nyquist diagrams for the various alloys studied are shown in Figure7. The EIS results showed higher impedances associated with the samples with the higher Mg-contents (x = 0.5 and x = 0.7), indicating a passive behavior for these alloys. The lowest impedances were associated with the alloy without Mg and supported the polarization results that indicated that this alloy presented the lowest corrosion resistance.Figure 7
Nyquist diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.The Bode phase angle diagrams in Figure8 show two time constants for all studied alloys with lower phase angles related to the alloys with low Mg contents (0.0, 0.1, and 0.3 at.%). For the alloys with 0.5 or 0.7 at.% Mg (without La), the time constant at high frequencies is seen at approximately 1 kHz, whereas for the other alloys, this time constant occurs at nearly 0.1 kHz. For all alloys, the second time constant is seen at approximately the same frequency, 0.1 Hz. The high frequency time constant is related to the surface oxide/hydroxide film, whereas the one at lower frequencies is associated with charge transfer processes. These results indicate that more protective surface films are formed on the alloys with the high Mg contents. This is most likely related to the refined grain microstructure associated with these alloys and shows that the substitution of La by Mg increases the alloy corrosion resistance mainly due to the formation of a more protective oxide film on their surface comparatively to that formed on the alloys with larger La contents. Passive surface films such as La(OH)3 and Mg(OH)2 have been reported in literature for La-Mg-Ni ternary alloy systems [24, 25]. Due to the very low reduction potentials associated with Mg and rare earth elements, such as La and Pr, in alkaline environments, these types of passive films are fairly stable [26].Figure 8
Bode phase angle diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5 and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.


### 3.3.2. Discharge Capacity

Figure9 shows the discharge capacity characteristics of the alloy electrodes with cycling. The range of measured discharge capacity values, limited to 250 mAh/g, could be attributed to superficial oxide formation during the preparation of the electrodes in the air. It can be seen that the electrodes can be easily activated within 2 cycles. Higher discharge capacity values were obtained for the Mg-free alloy with a maximum of 250 mAh/g and for x = 0.1 (maximum of 220 mAh/g). A significant decrease was observed for x = 0.3 (maximum ∼140 mAh/g), and a dramatic reduction in this property with higher amount of Mg was observed. Clearly, increasing the magnesium content on the alloys decreased the discharge capacity of the negative electrodes. From the structural viewpoint, the increasing amount of Mg decreased the presence of the phase similar to the LaNi5-type phase in the alloys, and the consequent increase of the abundance of the others observed phases (phases similar to the (La,Pr)Mg2Ni9 and MgNi2 phases). Notwithstanding the limitation of the discharge capacity showed experimentally by the LaNi5 phase (hexagonal, type CaCu5) [5, 27], the performance of this phase still overcame the (La,Pr)Mg2Ni9 and MgNi2 phases. The (La,Pr)Mg2Ni9 phases follow the structural model formed by the relation between the subunities (MgNi2)/(LaNi5) equal to 2. The subunity MgNi2 present (Laves phases, hexagonal type MgNi2) shows some slow performance for hydrogen storage very similar to that individually presented by the MgNi2 alloy (H/M∼0.33% in mass) [21]. Conversely, the hydride corresponding to the LaNi5 phase shows a hydrogen storage capacity H/M of 1.4% in mass [28]. Thus, comparatively, the higher abundance of the phase similar to the LaNi5 phase demonstrated to be beneficial to a higher discharge capacity of the electrodes. Furthermore, the refining of the alloys’ microstructure that followed the increasing substitution of La by Mg showed unfavorable to the discharge capacity. Counteracting this effect, the refining proved to be beneficial to the corrosion resistance, as indicated by the experimental results. Thus, magnesium addition proved to be favorable to the corrosion properties, but high amounts have shown to be deleterious to the discharge capacity of the alloy electrodes tested. The overall discharge capacities of the present as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys were somewhat superior to those obtained using mechanical alloying with a composition of La1−xMgxAl0.4Mn0.3Co0.3Ni3.8 (x = 0–0.2) [7]. On the other hand, better discharge capacities were obtained with La-rich mischmetal (MI) electrodes of MI1−xMgxAl0.10Mn0.10Co0.55Ni3.0 (x = 0.05–0.30) alloys [8]. These discrepancies can be attributed to the alloy preparation method, to testing conditions, and to the slight differences in the alloys compositions.Figure 9
Discharge capacity of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys versus cycle number.Figure10 shows the discharge potential curves of the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys. It is well known that the principle of operation of a Ni/MH battery is based on the ability of certain metals, alloys, or intermetallics to absorb hydrogen in a reversible way. The hydride formation/decomposition process occurs via electrochemical charge transfer reaction [5, 29]. It can be seen in Figure 10 that for the first three conditions of substitution of La by Mg (x = 0.0, x = 0.1, and x = 0.3) it is possible to identify two regions that are commonly present in the curves of discharge potentials. The relatively flat part is called potential plateau and corresponds to the discharge process controlled by charge transfer. On the other hand, the final part of the curve represents the striking decrease of the potential due to the depletion of hydrogen atoms from the electrode surface. Additionally, the discharge potential also decreases with the increase of the internal resistance of the alloy. The internal resistance of alloy generally includes contact resistance, charge transfer resistance, and diffusion resistance [30]. The La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0) electrode alloy presented the longest potential plateau, indicating more effective charge transfer process and lower internal resistance compared to the other studied alloys. Again, the substitution of La by Mg in the alloys studied, considering the structural changes that resulted, proved to be deleterious to the discharge capacity of the electrodes.Figure 10
The discharge potential curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.


## 3.3.1. Corrosion

Figure6 shows the anodic potentiodynamic polarization curves for the various tested alloys. At the corrosion potential, most alloys presented very low current densities (i), in the order of 10−5 to 10−6 A/cm2, typical of passive materials, but the lowest i value was related to the alloy with the highest Mg-content (x = 0.7). For the alloy without Mg (x = 0), the current density largely increased with overpotential showing that the passive film on this alloy had the lowest resistance. The passive films on the alloys with 0.6 and 0.4 at.% La content showed intermediate resistances, between that without Mg and that without La. These results show that electrochemical behavior of the alloys was highly dependent on their microstructures. The substitution of La by Mg that led to refinement in the grain structure also had a beneficial effect on their corrosion resistance.Figure 6
Anodic polarization curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys in 6.0 mol·L−1·KOH solution.The polarization curves show that from the corrosion potential up to 0.7 V the effect of the alloy composition and consequently its microstructure on the electrochemical behavior is clearly seen with the lowest current densities associated with the alloys with lower La contents, that is, increasing Mg concentration. At potentials of nearly 0.7 V, all alloys showed a current density increase, and from 0.8 V upwards the electrochemical behavior of the alloys with Mg-contents of 0.0, 0.1, 0.3, and 0.5 at.% was similar. On the other hand, for the alloy with total substitution of La by Mg, the current density values were lower than the other alloys in the whole potential range.The Nyquist diagrams for the various alloys studied are shown in Figure7. The EIS results showed higher impedances associated with the samples with the higher Mg-contents (x = 0.5 and x = 0.7), indicating a passive behavior for these alloys. The lowest impedances were associated with the alloy without Mg and supported the polarization results that indicated that this alloy presented the lowest corrosion resistance.Figure 7
Nyquist diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5, and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.The Bode phase angle diagrams in Figure8 show two time constants for all studied alloys with lower phase angles related to the alloys with low Mg contents (0.0, 0.1, and 0.3 at.%). For the alloys with 0.5 or 0.7 at.% Mg (without La), the time constant at high frequencies is seen at approximately 1 kHz, whereas for the other alloys, this time constant occurs at nearly 0.1 kHz. For all alloys, the second time constant is seen at approximately the same frequency, 0.1 Hz. The high frequency time constant is related to the surface oxide/hydroxide film, whereas the one at lower frequencies is associated with charge transfer processes. These results indicate that more protective surface films are formed on the alloys with the high Mg contents. This is most likely related to the refined grain microstructure associated with these alloys and shows that the substitution of La by Mg increases the alloy corrosion resistance mainly due to the formation of a more protective oxide film on their surface comparatively to that formed on the alloys with larger La contents. Passive surface films such as La(OH)3 and Mg(OH)2 have been reported in literature for La-Mg-Ni ternary alloy systems [24, 25]. Due to the very low reduction potentials associated with Mg and rare earth elements, such as La and Pr, in alkaline environments, these types of passive films are fairly stable [26].Figure 8
Bode phase angle diagrams of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0, 0.1, 0.3, 0.5 and 0.7) alloys tested in 6.0 mol·L−1·KOH solution.


## 3.3.2. Discharge Capacity

Figure9 shows the discharge capacity characteristics of the alloy electrodes with cycling. The range of measured discharge capacity values, limited to 250 mAh/g, could be attributed to superficial oxide formation during the preparation of the electrodes in the air. It can be seen that the electrodes can be easily activated within 2 cycles. Higher discharge capacity values were obtained for the Mg-free alloy with a maximum of 250 mAh/g and for x = 0.1 (maximum of 220 mAh/g). A significant decrease was observed for x = 0.3 (maximum ∼140 mAh/g), and a dramatic reduction in this property with higher amount of Mg was observed. Clearly, increasing the magnesium content on the alloys decreased the discharge capacity of the negative electrodes. From the structural viewpoint, the increasing amount of Mg decreased the presence of the phase similar to the LaNi5-type phase in the alloys, and the consequent increase of the abundance of the others observed phases (phases similar to the (La,Pr)Mg2Ni9 and MgNi2 phases). Notwithstanding the limitation of the discharge capacity showed experimentally by the LaNi5 phase (hexagonal, type CaCu5) [5, 27], the performance of this phase still overcame the (La,Pr)Mg2Ni9 and MgNi2 phases. The (La,Pr)Mg2Ni9 phases follow the structural model formed by the relation between the subunities (MgNi2)/(LaNi5) equal to 2. The subunity MgNi2 present (Laves phases, hexagonal type MgNi2) shows some slow performance for hydrogen storage very similar to that individually presented by the MgNi2 alloy (H/M∼0.33% in mass) [21]. Conversely, the hydride corresponding to the LaNi5 phase shows a hydrogen storage capacity H/M of 1.4% in mass [28]. Thus, comparatively, the higher abundance of the phase similar to the LaNi5 phase demonstrated to be beneficial to a higher discharge capacity of the electrodes. Furthermore, the refining of the alloys’ microstructure that followed the increasing substitution of La by Mg showed unfavorable to the discharge capacity. Counteracting this effect, the refining proved to be beneficial to the corrosion resistance, as indicated by the experimental results. Thus, magnesium addition proved to be favorable to the corrosion properties, but high amounts have shown to be deleterious to the discharge capacity of the alloy electrodes tested. The overall discharge capacities of the present as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys were somewhat superior to those obtained using mechanical alloying with a composition of La1−xMgxAl0.4Mn0.3Co0.3Ni3.8 (x = 0–0.2) [7]. On the other hand, better discharge capacities were obtained with La-rich mischmetal (MI) electrodes of MI1−xMgxAl0.10Mn0.10Co0.55Ni3.0 (x = 0.05–0.30) alloys [8]. These discrepancies can be attributed to the alloy preparation method, to testing conditions, and to the slight differences in the alloys compositions.Figure 9
Discharge capacity of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 alloys versus cycle number.Figure10 shows the discharge potential curves of the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys. It is well known that the principle of operation of a Ni/MH battery is based on the ability of certain metals, alloys, or intermetallics to absorb hydrogen in a reversible way. The hydride formation/decomposition process occurs via electrochemical charge transfer reaction [5, 29]. It can be seen in Figure 10 that for the first three conditions of substitution of La by Mg (x = 0.0, x = 0.1, and x = 0.3) it is possible to identify two regions that are commonly present in the curves of discharge potentials. The relatively flat part is called potential plateau and corresponds to the discharge process controlled by charge transfer. On the other hand, the final part of the curve represents the striking decrease of the potential due to the depletion of hydrogen atoms from the electrode surface. Additionally, the discharge potential also decreases with the increase of the internal resistance of the alloy. The internal resistance of alloy generally includes contact resistance, charge transfer resistance, and diffusion resistance [30]. The La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0) electrode alloy presented the longest potential plateau, indicating more effective charge transfer process and lower internal resistance compared to the other studied alloys. Again, the substitution of La by Mg in the alloys studied, considering the structural changes that resulted, proved to be deleterious to the discharge capacity of the electrodes.Figure 10
The discharge potential curves of the La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys.


## 4. Conclusions

From the structures and electrochemical properties of the as-cast La0.7−xMgxPr0.3Al0.3Mn0.4Co0.5Ni3.8 (x = 0.0–0.7) alloys investigated in this study, some conclusion can be summarized:(1)
The substitution of La by Mg in the hydrogen storage alloys refined the grain microstructure. Total substitution changed the structure of the grains from equiaxed to columnar. The investigated alloys consisted of LaNi5-, PrNi5-, LaMg2Ni9-, and PrMg2Ni9-type phases, and the lattice parameters and cell volumes of the phases decreased with increasing Mg content.(2)
The electrochemical results showed that the Mg addition leads to corrosion improvement likely due to a more protective oxide film formed on the refined grain microstructure of the substrate. The results also indicated that at nonpolarized conditions all alloys showed very low current densities, indicating a passive behavior. Hence, the corrosion resistance of the studied alloys is not a limiting property for their use as negative electrodes in Ni/MH batteries.(3)
Magnesium inclusion in the alloys studied proved to be deleterious to the discharge capacity, with the maximum discharge capacity decreased with the amount of Mg substitution, from 250 mAh/g (x = 0.0) to 12 mAh/g (x = 0.7), which corresponds to a fact that the abundance of a similar LaNi5 reference phase decrease with increasing Mg content.(4)
Based on the effect of substitution of Mg by La on the characteristics of the alloys and performance of the electrodes, it has been found that the La0.7Pr0.3Al0.3Mn0.4Co0.5Ni3.8 alloy could work as a base alloy for nonstoichiometry in the system AB5 together with the addition of small amounts of Mg aiming the improvement of Ni/MH battery electrodes.



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*Source: 9284943-2018-02-08.xml*