Process For The Storage Of Hydrogen Using A System That Strikes A Balance Between An Alloy Of Alkaline Metal And SIlicon And The Corresponding Hydride

Abstract

A process for the reversible storage of hydrogen, comprising bringing an alloy of alkaline metal and silicon into contact with gaseous hydrogen leading to the formation of the hydride or corresponding hydrides, comprises the use of at least one balanced system that corresponds to the formula:

Description

FIELD OF THE INVENTION

This invention relates to a process for reversible storage of hydrogen using new materials that are potentially advantageous for the storage of hydrogen.

PRIOR ART

Within the context of research of new energy systems, the development of processes for storage and transport of hydrogen is very important. Compounds with a lithium base that are used for storing hydrogen are known. Due to an excessive stability of the lithium hydride that makes it difficult to store hydrogen, it is necessary to use more complex lithium hydrides.

Document U.S. Pat. No. 6,514,478 B2 describes Li—Be—H-type hydrides. In a very general way, Patent Application WO 2004/05070 A2 describes the use of anisotropic nanostructures such as, for example, lithium nitride, able to be used in devices for storing hydrogen.

OBJECT OF THE INVENTION

This invention relates to a process for reversible storage of hydrogen using new materials that are potentially advantageous for the storage of hydrogen (theoretically more than 5% by mass) under the following conditions, defined by the pressure-temperature isothermal plateau:

270 K<T<370 K

and 1<P<10 atm (or about 0.1 MPa<P<about 10 MPa).

These new materials comprise a balanced system that is formed between an alloy of alkaline metal and silicon and hydride or the corresponding hydrides; they are of the type:

M_XMSiM_XMSiH_n

where M is selected from among Li, Na, or K and in which the atomic ratios X_M take on the following values:

X_Li=1

1≦X_Na≦3

1≦X_K≦2

n is the number of hydrogen atoms corresponding to the stoichiometry of the hydride or formed hydrides.

If the alloy that is formed between the alkaline metal and silicon is superstoichiometric, i.e., if the ratio X_Si that is defined by Si/M takes on values of from 1 to 4, the balanced system that is used is as follows:

MSi_XSiMSi_XSiH_2XSi+1

The new materials that are used from the hydrogen storage process are more particularly of the type:

Li_iSiLi_XLSiH₃,

Na_XNaSiNa_XNaSiH_n and

K_XKSiK_XKSiH_n.

n is the number of stoichiometric hydrogen atoms of the hydride or hydrides that are formed.

Atomic ratios X_M take on the following values:

X_Li=1

1≦X_Na≦3

1≦X_K≦2.

The invention also relates to new structures that correspond to formulas NaSiH₃ and LiSiH₃.

DESCRIPTION OF THE DRAWINGS

FIG. 1 plots the values of ΔE_hyd that are calculated and the experimental values ΔH_hyd of the literature.

FIG. 2 is the Van't Hoff diagram of simple hydrides using the calculated values of ΔE_hyd.

FIG. 3 is the X-ray diffraction spectrum of the NaSiH₃ crystalline structure.

FIG. 4 is the X-ray diffraction spectrum of the LiSiH₃ crystalline structure.

FIG. 5 is the Van't Hoff diagram for alloys of lithium and silicon.

FIG. 6 is the Van't Hoff diagram for the alloys of sodium and silicon.

FIG. 7 is the Van't Hoff diagram for the alloys of potassium and silicon.

DETAILED DESCRIPTION OF THE INVENTION

In the storage process according to the invention, the alloys of alkaline metal and silicon are brought into contact with gaseous hydrogen and thus lead to the formation of (a) corresponding hydride compound(s) (hydrogen absorption). By slightly increasing the temperature or slightly reducing the hydrogen pressure, the formed hydride restores the hydrogen (desorption). It is therefore a reversible storage process.

The hydrides at equilibrium with the alloys KSi, NaSi or LiSi or with the elements K, Li or Na and Si have improved thermodynamic properties for the storage of hydrogen.

The KSiH₃ structure is known, whereas the NaSiH₃ and LiSiH₃ structures are not inventoried in the ICSD and CRYSMET crystallographic bases, to which we have access. The NaSiH₃ and LiSiH₃ structures will therefore be resolved analogously to the KSiH₃ structure by the method of calculation that is described below.

• • The ICSD (Inorganic Crystal Structure Database) base is the property of the “Fachinformationszentrum Karlsruhe [Technical Information Center of Karlsruhe] (FIZ)” in Germany and the “National Institute of Standards and Technology (NIST)” in the U.S.A. (see also http://www.icsd.ill.fr//).
  • The CRYSMET base belongs to and is maintained by “Toth Information Systems,”Ottawa, and le Conseil national de recherches [National Research Council] of Canada.(ICSD and CRYSMET can be accessed within the MedeA interface marketed by Materials Design S.a.r.l., Le Mans (France)).

Many useful properties of a solid material can be derived directly from determining its chemical cohesion energy. This cohesion energy is intrinsically based on the chemical composition, the local atomic structure of the material, its electronic properties and all the physical properties that are derived therefrom. Quantum physics and more specifically the density functional theory (whose abbreviation DFT is obtained from the English “Density Functional Theory”) provide a reliable base for the quantitative prediction of structural, electronic and thermodynamic properties of an atomic, molecular or crystalline structure before any attempt at synthesis of the laboratory material (see: W. Kohn, L. J. Sham, Phys. Rev. A 140, 1133 (1965)). In particular, the formalism of the DFT, as it is implemented in many current quantum software applications, such as:

• • the “Vienna Ab initio Simulation Package” (VASP) (see: G. Kresse, J. Hafner, Phys. Rev. B 48 (1993) 13115; G. Kresse, J. Furthmüller, Phys. Rev. B 6 (1996) 15; as well as the address URL: http://www.cms.mpi.univie.ac.at/vasp/; references [1]);
  • “CASTEP” (see: http://www.tcm.phy.cam.ac.uk/castep/), and
  • “Gaussian” (see: http://www.gaussian.com),has as a central object the determination of the electronic wave function of a material that is simulated by an approximate solution to the famous Schrödinger equation. Access to the wave function makes possible the development of a predictive and quantitative methodology of the chemical bond in an atomic, molecular or crystalline structure.

In the search for new materials for the storage of hydrogen, the experimenters need to rely on the knowledge and a methodology of the chemistry of the solid. On the basis of thermodynamic concepts such as the formation enthalpy, the relative stabilities of the structures of materials can be quantified based on temperature and pressure conditions. The modern techniques of quantum calculation such as the DFT offer the advantage of relying on a minimal knowledge of empirical data for determining these same thermodynamic properties. Thanks to the knowledge of basic constants of physics, these techniques, thus often called “ab initio,” therefore make it possible to predict the energy stability and the physico-chemical properties of a crystalline structure defined by its composition and its crystallographic mesh, independently of any experimental approach. Moreover, these techniques make it possible to eliminate experimental uncertainties on the structure of a material.

The use of intermetallic hydrides as materials for storing hydrogen is based on the following chemical equilibrium:

$\begin{array}{cc}\frac{2}{n}M+H_2\to \frac{2}{n}{\mathrm{MH}}_n& \left(1\right)\end{array}$

where M represents the stable metallic phase being transformed into the stoichiometric hydride phase MH_n.

This hydride phase has a theoretical mass storage capacity that is equal to nMH/(nMH+MM)×100%, where MH is the molar mass of atomic hydrogen and MM is that of metal.

The thermodynamic characteristics of transformation (1) are described by a pressure-temperature isotherm. When the two hydride and metal phases co-exist, the isotherm has a plateau. Temperature T and equilibrium pressure P_eq of the plateau are determined by the Van't Hoff equation:

$\begin{array}{cc}\frac{2}{n}\ln \left(\frac{P_{\mathrm{eq}}}{P^0}\right)=\frac{\Delta H_{\mathrm{hyd}}}{\mathrm{RT}}-\frac{\Delta S_{\mathrm{hyd}}}{R}& \left(2\right)\end{array}$

where:

ΔH_hyd (or ΔS_hyd) represents the enthalpy variation (or the entropy variation) of transformation (1);

R=8.314510 J.mol⁻¹.K⁻¹ is the molar constant of the ideal gases, and

P⁰=1 bar is the standard pressure (or 0.1 MPa).

This approach can be generalized for hydrides of metal alloys, AB_x, in the following way:

$\begin{array}{cc}\frac{2}{n}{\mathrm{AB}}_x+H_2\to \frac{2}{n}{\mathrm{AB}}_xH_n& \left(3\right)\end{array}$

where A and B are two metal elements and x is the atomic ratio B/A in the alloy.

It is commonly recognized that the primary contribution according to the terms of entropic variation ΔS_hyd is the loss of entropy of the hydrogen molecule that passes from the gas phase in an adsorbed state into the solid state of the final hydride. The value of ΔS_hyd is known for being close to 130 J. K⁻¹.mol⁻¹ of H₂, regardless of the hydride (see: “Hydrogen-Storage Materials for Mobile Applications,” L. Schlapbach, A. Züttel, Nature 414 (2001) 353-358, reference [5]; and “Hydrogen Storage Properties of Mg Ultrafine Particles Prepared by Hydrogen Plasma-Metal Reaction,” H. Shao, Y. Wang, H. Xu, X. Li, Materials Science Engineering B 110 (2004) 221-226, reference [6]). Below, we retained this value. According to equation (2), also valid for reaction (3), the logarithm of the pressure at equilibrium, P_eq, varies linearly with the inverse of temperature T. The slope of the linear relationship is determined by ΔH_hyd. In the following examples, we will show, thanks to the Van't Hoff diagrams, the variations of the logarithm of P_eq based on 1/T (more specifically 1000/T for reasons of providing units). Such diagrams make it possible to identify potentially advantageous materials for storing hydrogen in a targeted range of P_eq and T.

Consequently, the prediction (by a reliable theoretical approach) is of major interest for the knowledge of temperature and pressure conditions in which the metal or alloy can be transformed into hydride. As ΔH_hyd is in general exothermic (for the stable hydrides), the slope is negative. The value of ΔH_hyd closely depends on the stability of the hydride relative to the metallic phase or to the alloy: the more thermodynamically stable the hydride, the more reaction (1) or (3) is exothermic.

The formation enthalpy of the hydride, ΔH_hyd, can be expressed based on the internal energy variation during hydrogenation, ΔE_hyd:

ΔE_hyd=E_ABxHn−E_ABx−E_H2  (4)

where E represents the internal energy of the hydride phases, metal, and the hydrogen molecule in gaseous phase. The internal energy of the material is linked to interactions between the atomic centers that constitute the material and the electrons. This energy is also often called electronic energy and is directly connected to the cohesion energy of the material. The expression of ΔH_hyd based on ΔE_hyd is as follows:

ΔH_hyd=ΔE_hyd+PΔV+ΔZPE+TΔc_p  (5)

where

Δc_p represents the calorific capacity variation between the hydride phase and the metal phase,

ΔZPE is the energy variation at the zero point between the hydride phase and the metal phase,

and ΔV is the variation of molar volume between the hydride phase and the metal phase.

The modern techniques for quantum simulation make it possible to calculate systematically the values of E_ABxHn, E_ABx, and E_H2, and therefore to derive therefrom the value of ΔE_hyd. For a given crystalline phase (known or unknown in an experimental way), the initial crystallographic structure is determined by the space group, the parameters of the primitive cell, and the atomic positions in the mesh of the primitive cell. For existing structures, the bases of crystallographic data, such as ICSD and CRYSMET, provide this information.

For the new structures (unknown or not totally resolved experimentally), the same standard description will be adopted in this invention. We will also add the simulation of the X-ray diffraction spectrum (DRX), commonly used experimentally for characterizing the observed structures.

For any structure (known or new), the process of rigorous simulation is adopted so as to determine the so-called basic state of the structure, i.e., the stable state of the structure. In this basic state, the values of E_ABxHn, E_ABx, E_H2, and ΔE_hyd are calculated. This process makes it possible in particular to determine the electronic wave function of the system by optimizing the crystalline structure for the hydride and metal solids and the hydrogen molecule, thanks to modern quantum simulation techniques at the DFT level, accessible in software such as VASP (see references [1] above). For this purpose, the following criteria are imposed during the calculation:

the criterion of convergence of the electronic energy should be set at 0.01 kJ/mol of primitive cell,

the criterion of convergence of the atomic positions and the volume of the primitive cell of the solid should lead to an energy precision of 0.1 kJ per mol of primitive cell,

the grid of points-k used to describe the Brillouin zone should be large enough to ensure a fluctuation of the electronic energy that is weaker than 0.01 kJ per mol of cell,

the size of the plane-wave base that is used or the precision of the base that is used should ensure a convergence of the electronic energy of more than 0.1 kJ per mol of primitive cell.

For the applications of storage of on-board hydrogen, an equilibrium temperature of close to 300 K (1000/T # 3.3 K⁻¹) is generally sought for a pressure that is close to 1 atm (about 0.1 MPa). Due to equation (2), this corresponds to a value of ΔH_hyd that is close to −39 kJ per mol of hydrogen. For this invention, and because of the precision of the simulation approach defined above, we will designate materials that are potentially advantageous for storing hydrogen, all the materials whose isothermal plateau verifies the following conditions:

270<T<370 K (or 2.7<100/T<3.7 K⁻¹)

and

1<P_eq<10 atm (or about 0.1 MPa<P_eq<about 10 MPa)  (6).

The target window that embodies this domain will be shown in all the Van't Hoff diagrams in the following examples.

According to the invention, the alkaline metal that is selected can be of “mixed” type, in which lithium, sodium and potassium can be substituted respectively by sodium and/or potassium, lithium and/or potassium and lithium and/or sodium.

According to the invention, the alloy can also comprise, in a proportion of less than 5% by weight, at least one light transition metal of groups 3 to 12 of the periodic table selected from among, for example, Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu and Zn.

The alloy of alkaline metal and silicon of the invention can come in solid or in dispersed form, obtained by, for example, grinding.

The process is applied to, for example, the storage of on-board, stationary or portable hydrogen.

The invention also relates to new structures that correspond to formulas NaSiH₃ and LiSiH₃, whose X-diffraction spectra are provided respectively in FIGS. 3 and 4.

EXAMPLES

Among the following examples, Example 1 is provided by way of comparison, and Example 2 illustrates the invention.

Example 1 (For Comparison)

Known Cases of Simple Hydrides

The diagram of FIG. 1 plots the values of ΔE_hyd that are calculated according to the process that is described above and the experimental values ΔH_hyd of the literature (see: “CRC Handbook of Chemistry and Physics,” 76^th Edition 1995-1996, David R. Lide Editor-in-Chief, CRC Press).

The crystallographic structures that are used are those of hydride and metal phases that are stable under conditions that are close to those set forth above in (6). They are recorded in Table 1.

TABLE 1
Simulated Structural Properties and Mass Capacity of Simple Hydrides.
	Crystallographic	Space	% by	Balance
Hydride	Reference	Group	Mass	Equation
LiH	ICSD.61751	FM3-M	22.37	2Li + H2 → 2LiH
NaH	ICSD.33670	FM3-M	8.00	2Na + H2 → 2NaH
BeH2	ICSD.84231	IBAM	18.17	Be + H2 → BeH2
MgH2	ICSD.26624	P42/MNM	7.60	Mg + H2 → MgH2
CaH2	ICSD.23870	PNMA	4.75	Ca + H2 → CaH2
YH2	CRYSMET.36093	Fm-3m	2.20	Y + H2 → YH2
TiH2	CRYSMET.38081	Fm-3m	4.01	Ti + H2 → TiH2
ZrH2	CRYSMET.39242	I4/mmm	2.15	Zr + H2 → ZrH2

The result of FIG. 1 shows that there is a linear relationship between the two basic values—experimental Δ_hyd and calculated ΔE_hyd—on a broad range of representative hydrides. These examples also show that the calculated value ΔE_hyd is a good thermodynamic descriptor for predicting thermodynamic properties of materials for the purpose of storing hydrogen. The final precision on the energy is on the order of 3 to 5%, which is in agreement with the method of calculation used and the process described above. This result implies that the contributions that are linked to terms Δc_p, ΔZPE and ΔV are negligible compared to the contributions of cohesion energies.

FIG. 2 represents the translation of these values to the Van't Hoff diagram by using the calculated values of ΔE_hyd. As is known experimentally, none of the simple hydrides of Table 1 (except for BeH₂, which exhibits other difficulties of operation) makes it possible to come close to the target window that is defined above, which makes it possible to consider the use of these materials for storing hydrogen.

For example, the case of magnesium hydride, which is used as a reference to the following, reveals that ΔH_hyd(MgH₂) is equal to −75.0 kJ per mol of H₂ (see references [2] and [3] above). The calculation provides a very close value, on the order of −70.2 kJ per mol of H₂. The equilibrium temperature at atmospheric pressure is 575 K experimentally (see reference [2]), which is much too high to be usable.

Example 2

Cases of Silicon Hydrides

A new family of materials that are based on silicon is potentially advantageous for storing hydrogen: KSiH₃, LiSiH₃ and NaSiH₃. They develop a high mass storage capacity (see Table 2). Only the KSiH₃ phase is inventoried in the database ICSD No. 65954 with space group PNMA. For the NaSiH₃ and LiSiH₃ phases, the structure of prototype KSiH₃ is retained (see Table 2).

TABLE 2
Structures of Silicon-Potassium, Silicon-Lithium
and Silicon-Sodium Hydrides
		Crystallographic
	Formula	Reference	Space Group	% by Mass
	KSiH3	CRYSMET.65954	PNMA	4.27
		Prototype KSiH3
	LiSiH3	CRYSMET.65954	PNMA	7.89
		Prototype KSiH3
	NaSiH3	CRYSMET.65954	PNMA	5.55

The X-diffraction spectra of the two new structures NaSiH₃ and LiSiH₃ are provided in FIGS. 3 and 4 respectively.

TABLE 3
Definition of the NaSiH3 Structure
Space Group PNMA
Parameters of the	a = 8.29396	b = 4.93395	c = 6.08397
Monoclinical Cell	α = 90.00	β = 90.00	γ = 90.00
Element	X	Y	Z
Na (4c)	0.16982	0.25000	0.16436
Si (4c)	0.05798	0.25000	−0.34777
H (4c)	−0.11812	0.25000	−0.26924
H (8d)	0.10891	0.47835	−0.18539

TABLE 4
Description of the Simulated LiSiH3 Structure
Space Group PNMA
Parameters of the	a = 8.53326	b = 4.71238	c = 5.30609
Monoclinical Cell	α = 90.00	β = 90.00	γ = 90.00
Element	X	Y	Z
Li (4c)	0.17456	0.25000	0.15957
Si (4c)	0.08540	0.25000	−0.35280
H (4c)	−0.06323	0.25000	−0.19195
H (8d)	0.16563	0.48443	−0.19051

The chemical balances considered and the calculated values of ΔE_hyd for the different materials are as follows:

2/3K+2/3Si+H₂→2/3KSiH₃ ΔE_hyd=−55.3 kJ/mol  (a)

2/3KSi+H₂→2/3KSiH₃ ΔE_hyd=−45.5 kJ/mol (x_K=1)

2/3Li+2/3Si+H₂→2/3LiSiH₃ ΔE_hyd=−34.8 kJ/mol  (b)

2/3LiSi+H₂→2/3LiSiH₃ ΔE_hyd=−7.3 kJ/mol (x_Li=1)

2/3Na+2/3Si+H₂→2/3NaSiH₃ ΔE_hyd=−36.2 kJ/mol  (c)

2/3NaSi+H₂→2/3NaSiH₃ ΔE_hyd=−31.9 kJ/mol (x_Na=1)

These balances can be expressed in the following general way by assuming a variable composition of M/Si=x_M (with x_M≧1):

2/(2+x_M)MSi+2(x_M−1)/(2+x_M)M+H₂→2/(2+x_M)MSiH₃+2(x_M)MH

In the case of a superstoichiometric material of Si (x_Si=Si/M encompassed between 1 and 4), the balance can be expressed in the following manner:

2/(2x_si+1)MSi+2(x_Si−1)/(2x_Si+1)Si+H₂→2/(2x_Si+1)MSi_XSiH_2XSi+1

This equilibrium involves the formation of a single hydride compound of the di-, tri- or tetra-silyl type of alkaline metals (M=Li, Na, K).

The KSi, LiSi and NaSi alloy phases are the structures that are identified in the CRYSMET base and provided in Table 5.

TABLE 5
Structures of Silicon Alloys Considered
		Crystallographic
	Formula	Reference	Space Group
	KSi	CRYSMET.84809	P-43n
	LiSi	CRYSMET.102320	I41/a
	NaSi	CRYSMET.80184	C2/c

The Van't Hoff diagrams that correspond to various preceding equilibria and for various elements are provided in FIGS. 5, 6 and 7 for the elements Li, Na and K, respectively. These diagrams show that the hydrides that contain silicon in the presence of lithium, sodium or potassium are likely to be advantageous materials with a high mass capacity for storing hydrogen under favorable thermodynamic conditions.

Table 6 below indicates the mass contents and hydrogenation enthalpy based on x_M as defined by the preceding chemical balances:

	TABLE 6
	XM	% by Mass	ΔEhyd (kJ/mol)
	LiXLiSi	1	7.89	−7.3
		2	8.70	−49.3
		3	9.27	−74.4
		4	9.70	−91.2
	NaXNaSi	1	5.55	−31.9
		2	5.12	−47.3
		3	4.90	−56.5
		4	4.76	−62.7
	KXKSi	1	4.27	−45.52
		2	3.63	−59.26
		3	3.32	−67.51
		4	3.15	−73.01

Claims

1. Process for reversible storage of hydrogen comprising bringing into contact an alloy of alkaline metal and silicon with the gaseous hydrogen leading to the formation of hydride or corresponding hydrides, characterized in that a balanced system is used and said system corresponds to the formula: MXMSiMXMSiHn

2. Process for reversible storage of hydrogen comprising bringing into contact an alloy of alkaline metal and silicon with the gaseous hydrogen, leading to the formation of hydride or corresponding hydrides, wherein a balanced system that corresponds to the formula: MSiXSiMSiXSiH2XSi+1

3. Process for reversible storage of hydrogen according to claim 1, wherein the alkaline metal that is selected is lithium and wherein the hydride phase that is involved in the balanced system is the LiSiH3 phase.

4. Process for reversible storage of hydrogen claim 1, wherein the lithium can be partially substituted by sodium and/or potassium.

5. Process for reversible storage of hydrogen according to claim 1, wherein the alkaline metal is selected from among sodium and potassium and involves the balanced system that corresponds to one of formulas: NaXNaSiNaXNaSiHn andKXKSiKXKSiHn.wherein the atomic ratios XM take on the following values: 1≦XNa≦31≦XK≦2n is the number of hydrogen atoms corresponding to the stoichiometry of the hydride or hydrides formed.

6. Process for reversible storage of hydrogen according to claim 1, wherein the sodium can be partially substituted by lithium and/or potassium.

7. Process for reversible storage of hydrogen according to claim 1, wherein the potassium can be partially substituted by lithium and/or sodium.

8. Process according to claim 1, wherein the alloy also comprises, in a proportion that is less than 5% by weight, at least one light transition metal of groups 3 to 12 of the periodic table selected from among Sc, Ti, V, Cr, Mn, Fe, Co, Ni, Cu and Zn.

9. Process according to claim 1, wherein the alloy of alkaline metal and silicon comes in solid form.

10. Process according to claim 1, wherein the alloy of alkaline metal and silicon is in dispersed form.

11. Process according to claim 1, wherein the alloy of alkaline metal and silicon is obtained by grinding.

12. Process according to claim 1, applied to the storage of on-board hydrogen.

13. Process according to claim 1, applied to stationary storage.

14. Process according to claim 1, applied to portable storage.

15. New crystalline structure that corresponds to formula NaSiH3 and belongs to space group PNMA.

16. New crystalline structure corresponding to formula LiSiH3 and belonging to space group PNMA.