Intermetallic Hydrides with High Dissociation Pressure

Introduction

An initial report on the ability of alloys and intermetallics to form compounds with hydrogen dates back to 1958, when Libowitz¹ showed that ZrNi easily and reversibly reacts with hydrogen forming ZrNiH₃. However, the birth of a new field, chemistry of intermetallic hydrides, is usually considered to be coincident with the discovery a decade later of hydrideforming compounds such as SmCo₅² and other rare earth AB₅³ and AB₂ ⁴ intermetallics.

Practical applications of intermetallic hydrides are based on their chemical interaction with hydrogen. In general, this reaction may be described by the following equation:

where M is a metal or an intermetallic compound. The rates of reaction for intermetallic compounds differ dramatically from those for individual metals. This peculiarity immediately brought attention to intermetallic hydrides as prospective materials for hydrogen storage and distribution. A majority of conventional materials absorb hydrogen at high rates at room temperature and low pressure. However, practical interest in these intermetallic hydrides is rather limited due to their relatively low reversible gravimetric hydrogen absorption capacity (1.4–1.9 mass.%). At the same time, in light of the greater safety of intermetallic hydrides compared to the hydrides of light metals, and the breadth of experience in applications, the development of new materials with a wide range of operating hydrogen pressures is of great practical interest. Moreover, current availability of novel high-pressure vessels (up to 250–350 atm), and development of 800 atm vessels, facilitate the investigation of high-pressure metalhydrogen systems. Indeed, storing hydrogen in a high-pressure vessel filled with a metal hydride combines the advantages of both compressed gas and solid state hydrogen storage techniques, thus increasing total capacity of the storage container by at least 10%. The metal hydrides based systems with high hydride dissociation/hydrogen desorption pressures are also extremely attractive for applications in high-pressure compressors and internal combustion engines as a part of cold-start ignition systems.

High-Pressure Device

The interaction of intermetallic compounds with hydrogen was studied in a new high-pressure apparatus in the temperature range between 243 and 573 K. A schematic drawing of the high-pressure system is shown in Figure 1.

The unit consists of a section for preliminary hydrogen purification and the high-pressure (HP) section. The preliminary purification section consists of a hydrogen source vessel and two hydrogen storage and purification units—one filled with an AB₅-type alloy (LaNi₅, Product No. 685933) and the second containing an AB₂-type alloy ((Ti,Zr)(V,Mn)₂, Product. No. 685941). This configuration prevents possible contamination of the HP generator system, containing vanadium hydride (VH₂), by impurities in hydrogen, which may poison the surface of VH₂, reduce its absorption capacity and, consequently, hamper its performance. The HP section consists of the HP-generator system containing VH₂, a sample holder, a buffer vessel, and two pressure transducers (D250 and D3000) with upper pressure limits of 250 and 3000 atm. Both the sample holder and the HP generator can be heated to high temperatures (up to 573 K) using muffle furnaces. The experimental temperature around the sample holder can also be maintained with a thermostat operating in the temperature range from 243K to 333 K. The data from pressure transducers and from thermocouples attached to the sample holder and the HP generator are collected by a computercontrolled data acquisition system. In order to perform correct hydrogen absorption and desorption calculations, we determined the volumes of all constituent parts of the system. These volumes were obtained in two ways—by calculations based on blueprint dimensions and by volumetric measurements after filling with water. The volume of the sample holder was found to be 8.929 mL. While calculating the total volume of the sample holder, the volume of the alloys and the relevant hydride were also taken into account. A typical sample size during our experiments varied between 15 and 20 g. The amounts of absorbed or desorbed hydrogen were calculated using a modified Van der Waals equation:⁵

1. [p+a(p)/Va][V–b(p)] = RT

where, a, b = pressure dependent coefficients (for p>1 atm);
p = pressure (atm);
T = temperature (K);
V = system volume (cm3);
R = universal gas constant (82.06 cm3∙atm/mole∙K).

Thermodynamic parameters of the desorption reaction were determined using the Van’t Hoff equation and fugacity values, corresponding to experimental pressure values:

2. RT ln(fp) = ∆H–T∆S

where, fp = fugacity;
∆H = enthalpy change;
∆S = entropy change.

Finally, the fugacity values were calculated using Equation 3 and real molar volumes obtained from Equation 1:

3. RT ln(fp) = RT ln p–^p∫₀(Vid–Vreal)dp

where, V_real = real absorbed/desorbed hydrogen molar volume
V_id = ideal absorbed/desorbed hydrogen molar volume

It is also worth noting that our system allows for conducting experimental studies of hydrogen absorption by intermetallics as well as investigating the behavior of various materials at high hydrogen pressures.

YNi5–H2 System

Interaction of hydrogen with AB₅-type intermetallics at high pressures has been reported.⁶ For LaCo₅, La_0.5Ce_0.5Co₅, and LaNi₅ it was shown that at high hydrogen pressures they form intermetallic hydrides of the approximate composition RT₅H₉ (R = rare earth metal; T = transition metal), which agrees with theoretical predictions.⁶ For our studies, we chose a YNi₅ alloy because of its unique properties. YNi₅ does not easily absorb hydrogen^7–9 at low pressures. However, as shown by Takeshita¹⁰, applying 1550 atm to the materials allows the synthesis of YNi₅H_3.5 hydride. Pressure-compositiontemperature (PCT) isotherms obtained led to a conclusion that the pressure applied was not sufficient to obtain a fully hydrogenated sample. The results of other authors¹¹ differed considerably from that of Takeshita.

Our studies showed that an active interaction of YNi₅ and hydrogen starts at pressures over 500 atm and the equilibrium hydrogen absorption pressure at 293 K is 674 atm while corresponding equilibrium desorption pressure is 170 atm. Hydride composition at 1887 atm corresponds to YNi₅H₅ (1.3 mass.% H₂). Absorption-desorption PCT-isotherms at the temperatures ranging from –20 to 80 °C are shown in Figure 2. Our data differs from those reported in reference 10, where there are two desorption plateaus at 300 and 1000 atm (293 K) and the hydride composition corresponds to YNi₅H_3.5. Our data also differs from the results reported in reference 11, where the dissociation pressure is only 12 atm and the hydride composition is YNi₅H_4.4.

The inconsistency in the numbers reported by different groups may be explained by very low hydrogen absorption and desorption rates observed. In our case, the time to reach equilibrium in the plateau region was between 2 and 4 hours; see Figure 3 which shows the readings of the pressure transducer in several consecutive hydrogen desorption steps.

A number of authors^7–9 compared hydrogen absorption properties of YNi₅ to other AB₅ alloys and concluded that peculiarities in its interaction with hydrogen can be explained neither by the low-temperature heat capacity nor the electronic structure, nor by the surface oxidation of YNi₅. In our opinion, the most possible explanation was given in reference, ⁸ where it was shown that among all binary AB₅-type intermetallic compounds YNi₅ has the lowest compressibility. Thus, the low volume of the YNi₅ unit cell could influence hydrogen absorption properties.

Using a lnP(H₂) vs. 1/T plot, we found the values of hydrogen desorption enthalpy and entropy of a YNi₅ hydride to be 21.86 kJ/mol H₂ and 115.8 J/K·mol H₂ respectively.

AB2–H2 Systems

As basis materials for these studies, we selected Laves phases ZrFe₂ and TiFe₂ with high hydrogen desorption pressures, which do not absorb hydrogen at relatively low pressures. It has been reported that using the ultra-high pressure of 10,000 atm, it is possible to synthesise a ZrFe₂ hydride.^12–14 Our studies showed that noticeable hydrogen absorption in the first absorptiondesorption cycle starts at approximately 800 atm without any preliminary activation. During subsequent cycling, absorption starts at lower pressures. Absorption equilibrium pressure in the first run has been found to be 1120 atm while in second and further cycles it decreased to 690 atm (Figure 4). The hydrogen content in the hydrogenated material at room temperature and 1800 atm is 3.5 H/formula unit. At the low temperature of 218 K and hydrogen pressure of 1900 atm, the material’s composition is ZrFe₂H_3.7. The isotherms shown in Figure 4 reveal an obvious hysteresis—at room temperature the absorption equilibrium pressure is about 690 atm, while the desorption one is only 325 atm.

Partial substitution of zirconium for scandium reduces the hydrogen desorption pressure of the hydride. Similar to ZrFe₂, Zr_0.5Sc_0.5Fe₂ and Zr_0.8Sc_0.2Fe₂ crystallize as C15 Laves phases. Hydrogen absorption in Zr_0.5Sc_0.5Fe₂ starts at ~100 atm without any preliminary activation. There is no significant hysteresis in this system, i.e. the absorption and desorption pressures are very close. Hydrogen content in the material at 295 K and 1560 atm reaches 3.6 H/formula unit (Figure 5).

The shape of the hydrogen absorption-desorption isotherms suggests the formation of two hydride phases in the Zr_0.5Sc_0.5Fe₂–H₂ system. At room temperature, the composition of the first phase (β1) is close to a dihydride and that of the second one (β2) corresponds to a trihydride (Table 1). Hydrogen desorption enthalpies and entropies have been calculated for both phases. Remarkably, the behavior of Zr_0.5Sc_0.5Fe₂ resembles that of the ScFe_1.8–H₂ system, where the stable monohydride and the much less stable ScFe_1.8H_2.4 are also formed.^15,16 In our case, however, substitution of half of the scandium for zirconium leads to a significant increase of stability of the lower hydride with an enthalpy of formation lower than that of the trihydride (Table 1).

Comparing hydrides ScFe_1.8H_1.8, Zr_0.5Sc_0.5Fe₂H_2.5 (second plateau) and Zr_0.8Sc_0.2Fe₂H_1.8 shows that the increase in zirconium content in the alloys leads to the decrease in its hydrogen desorption enthalpy. However, entropy change goes through a maximum at Zr_0.5Sc_0.5Fe₂H_2.5 (Table 1).

For Zr_0.8Sc_0.2Fe₂–H₂, hydrogen absorption also starts at 100 atm without activation. Hydrogen composition at room temperature (293K) and 1650 atm is Zr_0.8Sc_0.2Fe₂H_3.7 (Figure 6). Further cooling to 219 K with simultaneous increase in hydrogen pressure to 1730 atm results in maximum hydride composition corresponding to Zr_0.8Sc_0.2Fe₂H_3.8.

Partial substitution of titanium for scandium allowed us to synthesize the first pseudobinary intermetallic hydride in Ti_0.5Sc_0.5Fe₂–H₂ system. Remarkably, while Ti_0.8Sc_0.2Fe₂ does not absorb hydrogen even at pressures up to 2500 atm, at 223 K, the reaction between Ti0.5Sc0.5Fe2 and hydrogen starts at room temperature already at 100 atm without any preliminary activation (Figure 7). The hydrogen content of the hydride corresponds to Ti_0.5Sc_0.5Fe₂H_3.1 (2.0 mass%).

The room temperature equilibrium absorption and desorption pressures for this material are 195 and 175 atm accordingly. Cooling the hydrogenated material to below 223 K showed that no new hydride phase transition occurs. Hydrogen content at 217 K at 2700 atm is 3.4 H/f.u. (2.16 mass.%) and calculated thermodynamic parameters were are ΔH (kJ/ moleH2) = 17.7(2) and ΔS (J/K· moleH2) = 103.8(7)

Conclusions

Interaction of hydrogen with multi-component intermetallic compounds of AB5- and AB2-type were studied in the current work. Several new intermetallic hydrides with potential applications in high-capacity hydrogen storage have been identified and fully characterized using a gas-volumetric analytical technique.

Acknowledgements

This work was supported in part by General Motors Corp.