WO1996027697A1

WO1996027697A1 - Selective metal cation-conducting ceramics

Info

Publication number: WO1996027697A1
Application number: PCT/US1995/002871
Authority: WO
Inventors: Shekar H. Balagopal; John Howard Gordon; Anil V. Virkar; Ashok V. Joshi
Original assignee: Ceramatec, Inc.
Priority date: 1995-03-06
Filing date: 1995-03-06
Publication date: 1996-09-12

Abstract

Ceramic materials (24) are disclosed which have comprehensive characteristics of high ion-conductivity for alkali metal cations at low temperatures, high selectivity for alkaly metal ions, good current efficiency and stability in water and corrosive media under static and electrochemical conditions. Also disclosed is an electrochemical cell (20), the electrolyte (24) of which employs the disclosed ceramic materials, for use in the electrolysis of aqueous alkali salt solutions to form caustic.

Description

SELECTIVE METAL CATION-CONDUCTING CERAMICS

Technical Field: This invention relates to ceramic materials which are useful in many applications, but those which are particularly useful in electrolytic systems for simultaneous production of caustic and acids by electrolysis of an aqueous alkali metal (e.g., sodium) salt solution.

Background Art: Electrolytic systems for use in producing caustic from salt solutions have been disclosed. In such systems, various materials have been suggested for use as an electrolytic membrane positioned between an anolyte chamber and a catholyte chamber for transportation of ions therethrough. Such materials include ceramic materials alone, polymeric materials, and combinations of ceramic and polymeric materials.

The known advantage of polymeric materials as electrolytes in the electrolysis of salt solutions is their high conductivity and increased resistance to acidic and caustic environments resulting from the electrolytic process. The known disadvantage of polymers, however, is their low selectivity for ionic species. That is, polymers transport protons as well as alkali ions, such as sodium ions, the result of which is an inefficient operation of the electrolytic cell.

The known advantage of ceramic materials is their excellent ion-conducting characteristics and good selectivity under certain conditions. Nasicon (sodium fNa] super ion conductor, materials, such as Na₃Zr₂PSi₂O₁₂, have a known advantage over beta alumina, another sodium ion-conductor, in that Nasicon is comparatively stable in water while beta alumina is not. Further, Nasicon materials are comparable to beta alumina in superiority as sodium ion-conductors. The disadvantage of Nasicon- type materials is that some Nasicon-type materials are unstable in acidic and caustic environments due to some species of the Nasicon being particularly subject to attack by acids and the like. Further, ceramic materials have a lower ion conductivity at lower temperatures as compared to polymeric materials. Thus, the combination of polymeric and ceramic materials may provide a more suitable material for use in electrolysis of salt solutions.

Given the specific disadvantages of polymeric materials, however, and the additional labor and cost of producing ceramic/polymeric composite materials, it would be advantageous to provide a ceramic material having superior ion-conducting and selectivity characteristics, while being comparatively stable in water and acid/caustic environments.

DISCLOSURE OF THE INVENTION In accordance with the present invention, ceramic materials are disclosed which have comprehensive characteristics of high ion-conductivity for alkali metal cations at low temperatures, high selectivity for alkali metal ions, good current efficiency and comparative stability in water and corrosive media under static and electrochemical conditions. Ceramic materials of particular suitability are metal super ion conducting materials, or "mesicon" materials, which display the required characteristics. Nasicon-type materials are but one example of mesicon materials. While the ceramic materials disclosed herein are suitable for many applications, including gas generation and sodium sensor systems, the ceramic materials are described herein in connection with electrochemical cells which produce caustic from aqueous alkali salt solutions as an exemplar application.

The materials disclosed herein as being highly conductive and having high selectivity are those metal super ion conducting materials, i.e., mesicons, which are capable of transporting or conducting any alkali metal cation, such as sodium (Na), lithium (Li), potassium (K) or silver (Ag) ions. Various composition formulas have been described for metal super ion-conductors. For example, there are mesicon formulations which include Me₃Zr₂Si₂PO₁₂, where Me = Na, Li, Ag or K; MejGdSi₄θ₁₂ where Me = Ag, Li or Na; and

where A = Li, Na and K, and O < X ≤ 2. Included in the family of mesicon materials are Nasicon-type materials having various formulas, including

where 0 ≤ x ≤ 3 and Na₃M₂(PO₄)₃ where M = Sc, Cr or Fe. There are also so-called "Lisicon" materials, such as LiZr₂(PO₄)₃ and Li₃Zr₂Si₂PO₁₂.

Virtually all mesicon-type materials comprise species of compounds which give structural uniqueness to the material, and thereby enhance certain properties of the material or give rise to the disadvantages of the material. For example, the Nasicon-type material NasSmSi^O^ may generally include a certain number of moles each of Na₂O, Sm₂O₃ and SK of which, for example, Na₂O may be particularly subject to attack by H₂SO₄. Therefore, the mesicon-type materials of the present invention are selected to include the lowest concentration of species which are subject to corrosive materials while retaining structure which provides high conductivity.

While the ceramic materials disclosed herein encompass or include many formulations of mesicon materials, this disclosure concentrates on an examination of Nasicon-type materials for the sake of simplicity. The focussed discussion of

Nasicon-type materials as one example of mesicon materials is not intended to limit the scope of the invention, however.

Thermodynamic analysis suggests that Nasicon-type materials without the presence of phosphorus may offer the best formulation for achieving increased stability in corrosive (i.e., acidic or caustic) environments. However, the particular species of compounds which comprise the Nasicon-type material must be carefully selected to obtain the optimum lowest concentration of reactive species. Nasicon- type materials having the general formula NasRESύO^, where RE is Yttrium or any rare earth metal, are particularly suitable for electrolytic decomposition of sodium salts to produce caustic. However, other Nasicon-type and mesicon-type formulations which have the characteristics described herein are equally as suitable.

The stability in or resistance to corrosive media of the mesicon materials described herein may be enhanced by coating or treating the mesicon material with a very thin layer of glass material. The coating of glass, which preferably may be selected from the soda-lime-silicate variety, protects the underlying mesicon material from exposure to corrosive media, but does not significantly reduce conductivity.

Nasicon-type materials having the formula Na₅RESi₄Oι₂ contain rings formed by SiO₄ tetrahedra, twelve per ring, which are orthogonal to the c-axis. Sodium ions (Na⁺) move through channels between the rings. Conductivity of the material is a function of the ion size of Y or the rare earth metal selected. The species of

Nasicon-type materials having the formula Naj ESi₄Oι are, with slight exception for sodium silicates, not subject to attack by acids, such as sulfuric acid. Contrastingly, Na₃PO₄ is subject to attack by acids. Therefore, ^RESi^O^ materials are more resistant to corrosive environments than

formulas. In particular, Nasicon-type materials having the formula

have increased sodium ion conductivity and sodium ion selectivity compared to other sodium ion-conducting ceramics and polymers. The increased conductivity and selectivity of Nasicon-type materials of that formulation results from particular sintering procedures and temperatures which yield increased density of material. Further, the selected sintering techniques and temperature produce a single phase material which lessens or eliminate corrosion of the material since it appears that corrosion tends to occur at grain boundaries in the material. The Nasicon-type materials disclosed herein are useful as sodium-ion conducting electrolytes in electrolytic cells having a corrosion resistant container, a catholyte chamber, an anolyte chamber, an anode and a cathode. A sodium salt, such as an aqueous solution of sodium sulfate, is charged into the anolyte chamber. A solution of caustic is charged into the catholyte chamber. The solution may be dilute or concentrated. It is desirable to start with an electrolyte solution of some sort in the catholyte chamber since pure water is not a very good electrolyte. A general electrolytic reaction resulting from the use of the described electrolytic cell where M is a mono-valent cation and A is an anion with a charge of -x is as follows:

M_XA + 3/2x(H2O) → xMOH -I- H.A 4- V4xO₂ + V_H₂

More specifically, an overall electrolytic reaction resulting from use of the described electrolytic cell constructed with a sodium ion conducting Nasicon-type material as the electrolyte and using sodium sulfate is as follows:

Equation (1): Na₂SO₄ + 3H₂O → 2NaOH + H₂SO₄ + V2θ₂ + H₂ The half-cell reactions may be summarized as follows:

Equation (2): (anode) Na₂SO₄ -I- H₂O → 2Na⁺ + H₂SO₄ + 2e^" + ^» 2θ₂ Equation (3): (cathode) 2Na⁺ + 2H₂O + 2e^" → 2NaOH + H₂t

These reactions are electrolytic reactions, taking place under an induced current wherein electrons are introduced or are removed to cause the reactions. The reactions proceed only so long as a current is applied to the cell. Contrary to electrolytic reactions, galvanic reactions may occur when an applied potential to the cell is removed, which tends to reduce the efficiency of the electrolytic cell. It is preferred that only electrolytic reactions occur in the cell and that galvanic reactions be eliminated or, at least, greatly minimized. Nasicon-type materials, especially of the type described herein, have low (negligible) electronic conductivity, virtually eliminating any galvanic reactions from occurring when an applied potential or current is removed. Ceramic membranes of the present invention are those which have very mobile sodium, potassium, lithium or silver ions (high ionic conductivity), low electronic conductivity and comparatively high corrosion resistance. The cation conductive ceramic materials disclosed herein for use in electrolytic cells can be used successfully in the formation of caustic from the electrolysis of aqueous sodium salt solutions, including such solutions as sodium carbonate, sodium nitrate, sodium phosphate, sodium hypochlorite, sodium chlorite, and sodium perchlorate, and sodium organic salts. The ceramic materials disclosed herein are equally applicable for use in weak acid environments as in strong acid environments. An open-tube electrolytic cell is also disclosed for use in forming caustic from metal salt solutions.

T.T.TT.F Π SCRIFΠQN OF DRAWINGS FIG. 1 is an x-ray diffraction pattern of

FIG. 2 is an x-ray diffraction pattern of

FIG. 3 is a graph illustrating the conductivity of Na_JDySi₄O,₂ upon exposure to 10% solution of NaOH;

FIGS. 4a is a graph illustrating current density versus voltage in nitrate electrolysis using an electrolyte having the formula

FIGS. 4b is a graph illustrating current density versus voltage in nitrate electrolysis using an electrolyte having the non-stoichiometric formula Na_(J.j_β)Dy₍₁₊₈₎Si₍₄._2Λ)O₍,₂.5β₎ where δ = 0.02;

FIGS. 5a is a graph illustrating current density versus voltage in nitrate electrolysis using an electrolyte having the formula Na₃NdSi₄O,₂;

FIGS. 5b is a graph illustrating current density versus voltage in nitrate electrolysis using an electrolyte having the non-stoichiometric formula Na_(J.j_a)Nd₍₁₊j₎Si₍₄.₂j₎O₍₁₂.5S) where δ = 0.05;

FIGS. 6a is a graph illustrating current density versus voltage in chlorate electrolysis using

where δ = 0.02;

FIGS. 6b is a graph illustrating current density versus voltage in chlorate electrolysis using Na₍₅._Jβ)Dy_{(1 +«)}Si₍₄__2a)O₍,₂_.jx where δ = 0.02 under different conditions; FIGS. 7a is a graph illustrating current density versus voltage in chlorate electrolysis using Na₍₅.₅a₎Nd₍,_+β)Si_<4.₂,₎O₍ι₂.j_<0 where δ = 0.05;

FIGS. 7b is a graph illustrating current density versus voltage in chlorate electrolysis using Na_(J_jj₎Nd_(1+a)Si_<4.₂a₎O_α2.5β) where δ = 0.05; FIG. 8 is an x-ray diffraction pattern of NasDyS^O^ after exposure to a 1 % solution of sulfuric acid;

FIG. 9 is an x-ray diffraction pattern of NasDyS^O^ after exposure to a 10% solution of sulfuric acid;

FIG. 10 is an x-ray diffraction pattern of

after exposure to a 1 % solution of sulfuric acid;

FIG. 11 is an x-ray diffraction pattern of

after exposure to a 10% solution of sulfuric acid;

FIG. 12a is a schematic representation of the phase diagram of NasRES^O_jj materials illustrating incongruent melting; FIG. 12b is a schematic representation of an undesirable grain boundary phase microstructure;

FIG. 12c is a schematic representation of a desirable grain boundary phase microstructure;

FIG. 13 is a graph illustrating sintering optimization of

FIG. 14 is a graph illustrating sintering optimization of NajDySi₄O₁₂;

FIG. 15 is a schematic representation of an electrolytic cell with a flat plate electrolyte;

FIG. 16 is a schematic representation of a tubular electrolyte cell using mesicon-type material where the tube is closed at one end; and FIG. 17 is a schematic representation of a tubular electrolytic cell where the tube is open at both ends.

MODES FOR CARRYING OUT THE INVENTION The ceramic materials disclosed herein are particularly suitable for use in the electrolysis of aqueous alkali salt solutions because they have high ion-conductivity for alkali metal cations at low temperatures, high selectivity for alkali metal cations, good current efficiency and stability in water and corrosive media under static and electrochemical conditions. Comparatively, beta alumina is a ceramic material having high sodium ion conductivity, but is also known to be unstable in water and corrosive environments. Nasicon-type materials have equally high sodium ion conductivity in comparison to beta alumina, and have comparatively increased stability in water and corrosive environments. Nasicon-type materials are described with varying formulas having varying types of atoms included therein. Examples of general formulas of Nasicon-type materials include Na₁₊-Zr_xP₃._xSi₁-O,₂ where 0 ≤ x ≤ 3 and Na₃M₂(PO₄)₃ where M = Sc, Cr or Fe. However, thermodynamic analyses suggests that Nasicon-type materials which do not contain phosphorus may exhibit greater stability in corrosive environments. This appears to be true because certain species, including Na₃PO₄ and sodium silicates are more easily attacked by acids, such as H₂SO₄. Therefore, those Nasicon-type materials which do not contain phosphorus, or which contain significantly reduced concentrations of phosphorous-inclusive species are more suitable for use in electrolysis of aqueous sodium salt solutions. A particularly suitable Nasicon-type material has the formula NajRESi₄O,₂, where RE is Yttrium or any rare earth metal. Nasicon-type materials of that formulation are ringed structures formed by twelve SiO₄ tetrahedra. Sodium ions move through the channels formed between the rings. The ion conductivity through the material is a function of the ion size of the RE. Thus, for example, in Na_JSmSi₄Oi₂, σ = 0.1 (Qcm) ¹ at 200°C.

It should be noted that conductivity is generally greater at higher temperatures (e.g., _> 200°C). At lower temperatures (e.g., ≤ 200°C) the grain boundary phases may contribute to net resistance and are expected to lower the chemical resistance of the Nasicon-type materials to corrosive media. Minimizing the grain boundary phases leads to increased corrosion resistance.

contains 2.5 moles of Na₂O (35.72%), 0.5 moles of RE (7.14%), and 4 moles of SiO₂ (57.14%). The three binaries are NajO-REjO;, and Na₂O-SiO and REjO₃-SiO₂. No information is known on the Na₂O-RE₂θ₃ phase diagrams. However, with respect to Na₂O-SiO₂, the compounds 2Na₂O-SiO₂ (NajO- SiO₄), Na₂O-SiO₂ (Na₂SiO₃), and Na₂O-2SiO₂ (Na₂Si₂O₅) are known to exist. All of the sodium silicates are water soluble and are subject to attack by H₂SO₄. With respect to RE₂θ₃-SiO₂, the compounds

(REjSijO-) are known to exist where RE= Dy (dysprosium), Er (Erbium), Gd (Gadolinium), La (Lanthanum), Nd (Neodymium), Sm (Samarium) and Yb (Ytterbium), as well as for Y (Yttrium).

The free energies of reaction of Na₃PO₄ and Na₂SiO₃ with H₂SO₄ are as indicated below. The standard free energies at 25 °C of the following compounds are:

Material ΔG° fkcal/mole.

Na₂SiO₃ -341.00

Na₃PO₄ -427.00 H₂SO₄(aq) -178.00

H₂SiO₃ -260.00

H₃PO₄ -268.00

Na₂SO₄ -303.00 For the reaction

2Na₃PO₄ + 3H₂SO₄ → 3Na₂SO₄ + 2H₃PO₄ (i) the standard free energy change is

ΔGi° = 3 x (-303) + 2 x (-268) - 2 x (-427) - 3 x (-178) = -57 kcal. That is, reaction (i) is favored. For the reaction Na₂SiO₃ -I- H₂SO₄ → Na₂SO₄ + H₂SiO₃ (ϋ) the standard free energy change is

ΔG_»° = - 303 - 260 + 341 + 178 = - 44 kcal. Reaction (ii) will also occur.

With the foregoing in mind, it can be seen that Nasicon-type materials having the formula Na,_+xZr_xP₃._xSi_xO_ι2 contain species which are less thermodynamically favorable because of the phosphorous content. However, even with Nasicon-type materials having the formula Na₅RESi₄O₁₂, it is essential to minimize the thermodynamic activity of Na₂SiO₃. Lower activities of sodium silicates can be achieved by making compositions that are slightly rich in rare earth silicates and slightly poor in sodium silicates (or oxide) while maintaining the structure. Thus, in the pseudoternary Na₂O-RE₂θ₃-SiO₂, the objective is to make samples of compositions slightly away from the NajO apex. The compositions described herein are selected with sufficiently low species activity of

so that the materials are not subject to attack by H₂SO₄ or other corrosive media. The Na₅RESi₄O,₂ Nasicon-type materials present a rhombohedral structure

(which can be indexed as a hexagonal). The possible choices for RE in these materials includes Yttrium and any rare earth metal. Of that choice of atoms, those which have larger ionic radii are more suitable as part of the Nasicon-type compound because an increase in ionic radii is consistent with larger channel size in Na_JRESi₄O₁₂ and, therefore, an increase in ionic conductivity. Correspondingly, the larger the ionic radii and the higher the ionic conductivity, the more conductive is the material at lower temperatures.

The ionic radii of the larger ionic rare earth metals are r_γ = 0.893 A, r-^ = 0.908 A, r-_d = 0.938 A, r_Sm = 0.964 A, r_Nd = 0.995 A, and r^ = 1.016 A. Lutetium appears to be less suitable due to its smaller radius, namely r^, = 0.85 A. Nonstoichiometry may be described as deviation from stoichiometry along the

Na₅RESi₄O₁₂-RE₂O₃.2SiO₂ joinder. Samples were made with the following compositions with δ as the measure of deviation from stoichiometry.

(Na_JRESi₄O₁₂)₍₁._i)(RE₂O₃.2SiO₂)_e or Na₅.₃₄₎RE_{(1 +β)}Sι₍₄_₂j)O i₂.jj)

The above assumes a pseudobinary between NajRESi₄O_I2 and RE-O₃.2SiO₂. Thus, if a compound or a phase is made in such a way that δ is a maximum possible, the thermodynamic activity of

will be the least possible in the conducting phase where the generic formula may still be referred to as "NasRES^O, . As δ increases within the stability of the "NasRES^O, phase, the activity of Na₂O decreases and thermodynamic stability in acidic media increases.

A process for manufacturing a Nasicon-type material having the prescribed characteristics is as follows.

1. Na₂CO₃, SiO₂, and RE^ precursors are mixed in desired proportions. As noted, the objective is to make compositions with several nonzero values of δ.

2. Powder mixtures are calcined at 900°C for 12 hours.

3. The calcined powders are milled in an attritor mill for 6 hours.

4. Discs and pellets are green-formed by die-pressing followed by isostatic pressing.

5. Discs and pellets are sintered over a range of temperatures between 925 °C and 1150°C for up to 8 hours. 6. Sintered discs and pellets are annealed (selected samples) over a range of temperatures between 875 °C and 1130°C for up to 6 hours. Example I describes a specific process for formulating Na₅NdSi O₁₂.

Example I

Na₂CO₃, and SiO₂ were used as the precursors. Powder mixtures containing Na₂CO₃,

and SiO₂ were made in a molar proportion of 5 moles Na₂CO₃, 1 mole of Nd₂O₃, and 4 moles of SiO₂. Powder mixture was ball-milled in methanol for 24 hours. The slurry was dried at 60^CC for 12 hours, passed through 18 mesh screen, and calcined at 900°C for 12 hours. The calcined powder was characterized with regards to weight loss (gravimetry), phase(s) present (X-ray diffraction), and particle size and surface area (BET). The calcined powder was attritor-milled to reduce the particle size and render the powder sinterable. Powder was again characterized with respect to surface area and particle size distribution. Green pellets were uniaxially pressed at 137.9 x 10⁶ Newtons per square meter (20 ksi) and isostatically pressed at 172.4 x 10⁶ Newtons per square meter (25 ksi). The pellets were fired at 1000°C for 4 hours. The sintered samples were blue in color. The bulk density of the samples was determined to be approximately 3.00 gms/ml. The samples were impervious indicating that they had sintered to the stage of closed porosity. The melting temperature of the samples was determined to be approximately 1050 °C.

Samples of various compositions were fabricated substituting Y, Dy, Gd, Sm, Nd, and La for RE. It has been reported that the NajRESi₄O_π rhombohedral structure is unstable for ionic radii which are too large. Specifically, it has been reported that the rhombohedral structure is unstable with Nd and La. X-ray diffraction (XRD) work demonstrates this to be the case in that the XRD patterns of NajNdSijOu and NasLaS^O^ are different from those with other RE ions and are also different from each other. Both samples, however, densified during sintering and yielded dense pellets which could be further characterized with respect to electrical conductivity and electrochemical characterization.

The X-ray diffraction (XRD) traces of

are different from each other as shown by FIGS. 1 and 2, respectively. The XRD trace of

is the same as that reported for many other

and is of -li¬ the Nasicon-type. However, that of

is different. As will be discussed later, ionic conduction characteristics of Na_JNdSi₄Oι₂ are excellent for application, both at low and high temperatures. NasNdS^O^ has a different, at present unknown, structure.

is conductive while

appears to be an insulator. The conductivity of

NasNdS^O^ at 70°C was measured to be approximately 2.8 x 10^"3 (Ωcm)^"1 while that of NajLaSi₄Oi₂ was approximately 2.4 x 10^"6 (Ocm) ¹.

and

all have a structure similar to each other.

ELECTROCHEMICAL TESTING

Various

electrolyte materials have been evaluated in electrochemical cells for the decomposition of Na₂SO₄, NaClO₃, and NaNO₃, particularly NasDyS^Oπ, Na₅SmSi₄O,₂, and Na^NdS^O^ as the electrolyte materials. Testing was also done with NaOH solution in water for the purpose of determining the conductivity without the complication of corrosion effects.

The NajRESi₄O,₂ electrolytes were found to be electrochemically stable in sodium hydroxide solution. Taking advantage of this characteristic to determine the sodium ion conductivity of these materials with the absence of any corrosion effects, current was measured as a function of voltage when both anolyte and catholyte were 10% NaOH solutions. FIG. 3 shows experimental results for

which was sintered at 1125° C for 8 hours. The experiment was conducted at 70°C. From the slope of the curve in FIG. 3, the conductivity of the material was calculated to be 0.011 (ohm-cm)^"1. Conductivity of that magnitude is extraordinarily high for a solid material at relatively low temperature. The maximum current density at 5 volts was observed with material and was about 3.5 kA/m² which is about half that of Nafion^®, a polymer useful as an electrolyte. The Na_JRESi₄O₁₂ materials typically exhibited 95 to 100% current efficiency due to excellent selectivity. By contrast, Nafion^® shows substantially lower (approximately 60%) current efficiency. Table 1 gives a summary of conductivity, electrochemical testing and comparison with Nafion^®. It can be seen that although phosphate containing Nasicon-type material is a suitable electrolyte, the Nasicon-type materials containing no phosphate have substantially higher conductivity when properly optimized through processing as described further hereinafter. In addition, they generally have higher selectivity toward sodium ions over protons and, thus, current efficiency is higher.

TABLE 1

id* = Current density assuming 5.0V total, 0.5mm membrane, zero gap, 0.85V anode overpotential, 0.5V cathode overpotential, 2.06V decomposition voltage

FIGS. 4-7 show current density vs. voltage for nitrate and chlorate splitting with Na₃DySi₄O,₂ and Na₅NdSi₄O₁₂ electrolytes. Current densities 1.6 kA/m2 were noted with negligible corrosion. All of the

materials exhibited corrosion in H^O^

CORROSION IN H.SO.

Experiments were conducted to determine the stability of the NasRES^O^ phase in sulfuric acid. Samples of Na₅RESi₄O₁₂ material were subjected to varying concentrations of sulfuric acid, namely 0.1 %, 1.0% and 10%, at a temperature of 70°C for 24 hours. The suggested reaction is illustrated in the following equation: 2Na₅RESi₄O,₂ + 5H₂SO₄ → 5Na₂SO₄ + E₂θ₃.2SiO₂ + 6SiO₂ + 5H₂O

The calculated free energy of the reaction is: ΔG° = -2,067 + ΔC_RE-_OS^_JOZ

Now, 2ΔG°_Ni3RESi40_₂ = 5ΔG°_Nt20 + 6ΔG°_si02 + ΔG° RE_03.2s.02 + Δ°. Thus, (I) becomes: ΔG° = -2,067 = 5ΔG°_Nt20 - 6ΔG°_sio2 - Δ° or

ΔG° = -465 - Δ° = -465 + | Δ° | Kcal/mol. If ΔG° < 0 then the reaction may occur spontaneously. It was observed that the NasRESitOπ material reacts with H₂SO₄ when the ceramic material is in a powder form. X-ray diffraction patterns illustrating the effect of sulfuric acid treatment of

respectively, in acid concentrations of 1 % and 10% are shown in FIGS. 8-11. Thus, | Δ° | < 465 Kcal/mol. However, the rate of corrosion on dense samples is expected to be much slower than that on powder. Further, reaction of with H₂SO does not appear to form RE₂θ₃.2SiO₂ or

Thus, the material which remains after treatment with sulfuric acid contains some sodium, and Na₅RESi₄O,₂ materials do not totally disintegrate.

The corrosion resistance of the Na_jRESi₄O,₂ for the intended application can be further enhanced by depositing a thin layer of a glass which is known to be resistant to attack by H₂SO₄. A layer of glass may be positioned on the

electrolyte as depicted below. A number of different types of glass material are suitable for use, and particularly those which include sodium in their compositions. Soda-lime-silicate glasses are particularly suitable. The deposition of a glass coating may be achieved by a number of methods, including dip-coating, slurry coating, sputtering, MOCVD (metal organic chemical vapor deposition), and sol-gel. Of these, the latter two methods are particularly suitable because a very thin deposition layer (about 1000 A) of glass is possible with those methods.

The specific resistance of the composite may be shown as , r = p_{elcctr<Λ ι}. d + p_gUss δ, where d = thickness of the electrolyte NajRESi₄O₁₂, δ = thickness of glass, _ekcttoi_ytt = resistivity of

and p_gUts = resistivity of the glass. The anticipated thickness of the glass coating on the electrolyte is δ « 1 ,OOθA. The unit of specific resistance is (Qcm²).

Deposition of the glass coating by the sol-gel method was conducted as follows:

Example π A sodium conducting glass was prepared to have the following end composition: 46% Na₂OH, 43% SiO₂, and the balance ZrO₂. A dry environment for all handling of precursor materials was required. Tetraethyl orthosilicate (Si(OC₂H₅)₄), sodium ethoxide (CjHsONa), and zirconium (TV) ethoxide (Zr(OC₂H₅)₄), were mixed in the proper stoichiometric ratios with 50% dried ethanol. Disks of Nasicon-type material, having a thickness of 0.5 mm, were thoroughly cleaned and dried, and were then dipped into the metal alkoxide mixture and were slowly removed. Subsequently, the disks were exposed to room humidity (40%RH) for 24 hours. The disks were then heated to 100°C for 1 hour, then heated to 400°C for 1 addition hour to complete the drying. Glass compositions which appear to be particularly suitable for use as coatings on ceramic electrolytes include Na₂O(46.0%), SiO₂(43.0%), ZrO₂(11.0%); Na₂O(42.0%), SiO₂(45.0%), ZrO₂(5.0%), A1₂O₃(8.0%); Na₂O(37.5 %), SiO₂(50.0%), ZrO₂(12.5%); and Na₂O(45.0%), SiO₂(50.0%), B₂O₃(5.0%). IMPROVING CONDUCI-VπΥ AT LOW TEMPERATURES . «70°C.:

Improved conductivity at low temperatures (about 70 °C) minimizes the power requirements of the electrolytic cell. Also, most of the corrosion is expected to occur by dissolution of grain boundary phases. It is thus desirable to ensure that grain boundaries are clean. It appears, based on sintering studies, that some incongruence in melting occurs at the boundary phases of Na_sRESi₄O₁₂ materials, as shown schematically in FIG. 12a. In order to remove the grain boundary phases, it is desirable to anneal sintered materials at lower temperatures (about 800°C to 900 °C) so that single phase materials are formed. Highest possible conductivity is achieved, therefore, by improving the density of the material through selection of certain powder characteristics, by controlling sintering conditions, and by assuring single phase compositions through annealing procedures. The improved conductivity of the Nasicon-type materials was brought about by an optimization of the material, by the following steps: 1) The particle size of calcined materials were thoroughly reduced to insure dense packing of powders prior to sintering.

2) The melting range of the materials was determined experimentally to determine the upper limit for sintering and annealing.

3) The effects of sintering temperature and hold time on density (inversely related to porosity) were determined to find conditions which achieved low porosity. Only materials which were at least 95% of theoretical density were considered for further testing. FIGS. 13 and 14 show the results of this kind of experimentation. As sintering temperatures and holding times increase, the opportunity to separate out a second phase increase. FIG. 12a shows how at a lower temperature, a single phase is in equilibrium while at a higher temperature, below the melting range, two phases are in equilibrium at the same composition. While it is desirable to increase the density, it is undesirable to separate out a second phase as shown in FIG. 12b. It is preferable to increase the sintering temperature and time to increase the density but still maintain a single phase microstructure as shown in FIG. 12c.

4) X-ray diffraction spectrometry was used to verify that the materials remained in a single phase. -15/1-

5) Finally, the materials were tested as ionic conductors in electrochemical cells to verify which materials and processing techniques yielded the

-16- highest conductivity. Table 1 , above, indicates the sintering temperatures found to give good results and the material conductivity measured.

The improvement in density which results from various sintering temperatures is demonstrated in FIGS. 13 and 14 for

and Na.DySi₄O_I2, respectively. The ceramic materials of the present invention, having characteristics of high alkali metal ion-conductivity, high selectivity, low electron conductivity, good current efficiency and stability in water and corrosive media, are particular suitable in electrolytic systems as an electrolytic membrane 10 which divides an anolyte chamber 12 from a catholyte chamber 14 in which are positioned, respectively, a cathode 16 and an anode 18, as shown in FIG. 15.

Membranes of mesicon-type material as described above may be formed by conventional ceramic processing techniques. Such membranes may be in the form of very thin sheets (tape cast) supported by underlying porous ceramic plates (e.g. , porous Nasicon or alpha alumina), or by porous electrodes, or in the form of thicker sheets (plates) or tubes. A cell employing tubes of Nasicon-type material is illustrated in FIG. 16 wherein concentrated caustic is formed inside the tubes. The anolyte and catholyte chambers may be reversed.

An alternative electrochemical cell structure is illustrated in FIG. 17 which shows how tubes of mesicon materials may be open at both ends and may be used for generating metal hydroxide, such as sodium hydroxide, from a metal salt, such as sodium sulfate, in a continuous manner. A cell container 20 holds the anolyte 22 which is an aqueous solution of the metal salt. Metal salt and water flow into the cell container in a continuous or semi-continuous manner as acid bearing anolyte is removed in a continuous or semi-continuous manner. Tubes 24 constructed of the metal ion conducting sohd electrolyte are positioned such that the upper ends 26 are vented to atmosphere or to a hood while the bottom ends 28 of the tubes protrude through openings in the container floor 30. A seal 32 between the container floor 30 and the tubes 24 prevent anolyte from seeping out. The solid electrolyte tubes connect into a header pipe 34 or manifold or chamber below the cell container 20. Metal hydroxide and water flow into the header 34 in a continuous or semi- continuous manner while metal hydroxide solution flows out with a concentration greater than the initial concentration. Hydrogen generation at the cathodes 36 located within the tubes causes a gas lifting pumping action which circulates -16/1- catholyte 38 within the tubes with the solution in the header 34. Oxygen generated

-17- at the anodes 40 located outside of the tubes similarly causes circulation. A float valve or weir arrangement (not shown) is utilized such that the hydraulic level of the catholyte 38 is nearly the same as the anolyte.

In FIG. 17, the electrodes 36, 40 are shown to be adhered to and supported by the electrolyte tubes 24. However, they could be located off the tube surface and supported separately. Also the catholyte and anolyte positions could be reversed. For example, the catholyte could flow in the cell container while the anolyte could flow in the header.

From an energy efficiency standpoint, very thin ceramic membranes are preferred. These have the smallest ohmic resistance and energy loss. Thin sheets of Nasicon-type material, for example, may be formed by tape casting. Sheets as thin as about 25 micrometers to 0.5 mm are readily producible. Such thin sheets are preferably supported on or between porous structural supports. Such structural supports may be the electrodes or porous ceramic sheets or plates. The porosity of such ceramic supports is preferably quite high so that the liquid solutions on either side of the supports may be in intimate contact with a large area of the electrolytic membrane. Porosity, as a percent of total volume for electrolyte supports, ranges from about 30% to about 90% porosity.

Ceramic electrolytes of the type disclosed herein may be vapor deposited (sputtered or plasma sprayed) onto a porous substrate to form membranes which are very thin, e.g. about 5 μ or even thinner. The porous substrate must have similar thermal expansion and good bonding with the membrane as well as good mechanical strength. If electrode materials are utilized as structural supports, then similar characteristics for these must be present. The mesicon materials described herein have characteristics of high metal cation conductivity, high cation selectivity, and comparative stability in aqueous and corrosive media. The described characteristics render the disclosed mesicon materials suitable for use in many applications, including gas generation, and as a sodium sensor in a system such as is described in U.S. Patent No. 5,120,422.

Claims

-18- CLAIMS What is claimed is:

1. A metal cation-conductive ceramic material for use in corrosive, aqueous environments, said ceramic material having high metal cation ion conductivity at low temperatures, high selectivity for said metal ions, good current efficiency and stability in water and corrosive media.

2. The ceramic material of claim 1 wherein said metal super ion conductor comprises a reduced number of species which are reactive to acids.

3. The ceramic material of claim 2 wherein said metal super ion conductor is a sodium super ion conductor.

4. The ceramic material of claim 3 wherein said sodium super ion conductor has the formulation NasRES-ύO.j, where RE is a rare earth metal or

Yttrium.

5. The ceramic material of claim 4 wherein said sodium super ion conductor is Na₅NdSi₄O₁₂.

6. The ceramic material of claim 4 wherein said sodium super ion conductor is Na₍₅._J6)Nd_{(I +δ)}Si₍₄.₂j,O(i₂.58), where 0 ≤ δ ≤ 0.05.

7. The ceramic material of claim 4 wherein said sodium super ion conductor is NajDySi₄O,₂.

8. The ceramic material of claim 4 wherein said sodium super ion conductor is Na₍₅._Jδ)Dy_{(1 +}j₎Si₍₄.₂j₎O₍₁₂.ja₎, where 0 ≤ δ ≤ 0.02.

9. The ceramic material of claim 4 wherein said sodium super ion conductor is Na₍₅._ja)Sm_{α +i)}Si_<4.₂j)O .₅a₎, where 0 ≤ δ ≤ 0.02. -18/1-

10. The ceramic material of claim 3 wherein said sodium super ion conductor has the formulation Na_1+xZr_xP₃__xSi_xO₁₂, where 0 ≤ x ≤ 3.

-19- 11. The ceramic material of claim 2 wherein said metal super ion conductor has the formula

where Me is selected from the group consisting of Ag, Li, Na or K.

12. An electrolyte for use in an electrochemical cell used for electrolysis of aqueous alkali metal salt solutions to form caustic, said electrolyte comprising a ceramic material being a metal cation conductor having high metal cation conductivity at low temperatures, high selectivity for said cations, good current efficiency and stability in water and corrosive media.

13. The electrolyte of claim 12 wherein said metal cation conductor has the formula

where Me is selected from the group consisting of Ag, Li, Na or K.

14. The electrolyte of claim 13 wherein said sodium super ion conductor has the formulation Na₅RESi₄O,₂, where RE is a rare earth metal or Yttrium.

15. An electrochemical cell containing an aqueous catholyte media, an acidic anolyte media and a solid electrolyte comprising a super cation conductor of the formula Me₅ReSi₄O,₂, wherein Me is a metal selected from the group consisting of sodium, potassium, lithium and silver, and Re is Yttrium or a rare earth metal.

16. The electrochemical cell of claim 15 wherein said super cation conductor is

17. The electrochemical cell of claim 15 wherein said super cation conductor is Na_sDyS^O^.

18. A ceramic material having the formula NasNdS^O^, said ceramic material having high sodium ion conductivity and high selectivity of sodium ions, and being stable in aqueous and corrosive media. -20-

19. A ceramic material having the formula

said ceramic material having high sodium ion conductivity and high selectivity of sodium ions, and being stable in aqueous and corrosive media.

20. An electrolyte for use in an electrochemical cell, said electrolyte comprising a substrate of mesicon material which has high conductivity for metal cations and high selectivity for said metal cations and which is comparatively stable in aqueous and corrosive media, and further including a glass coating on said substrate of mesicon in an thickness which permits cation conductivity through said substrate.