OXYGEN SENSOR, HIGH TEMPERATURE FUEL CELL AND OXYGEN SEPARATOR

Abstract: Oxygen ion conducting ceramic materials, represented by the formulas Ni(Nb1-xMx)2O6-x and Ni2(Nb1-xMx)2O7-x, wherein M is selected from the group consisting of Zr<+4>, Ti<+4>, Sn<+4>, Sm<+4>, Hf<+4> and Ce<+4> and x is a value from 0 to 0.2. To provide better performance, lower threshold operating temperatures, and greater resistance to thermal shock, these materials, along with Bi2O3 in solid solution with Y2O3 or Nb2O5, may be used in a device for use as an oxygen sensor, fuel cell or oxygen separator. The device includes at least one layer (20) of the ceramic material with layers (22, 26) of a porous metallic conductor arranged on either side to form a body (18). An electrode (30) connects one layer (22), and a second electrode (32) connects the opposite metallic layer (26). Depending upon the use for the device, oxygen ions diffusing through the ceramic layer (20) causes a voltage signal to appear across the electrode (30, 32), or a voltage signal applied across the electrodes causes ions to diffuse through the ceramic layer.

Description: OXYGEN SENSOR, HIGH TEMPERATURE FUEL CELL AND OXYGEN SEPARATOR Technical Field The present invention relates to oxygen sensors, fuel cells and oxygen separators. More particularly, the invention relates to ceramic materials and structures for sch devices. Background Art Oxygen sensing devices are generally well known. One common type of presently known sensing device functions by monitoring the EMF developed across an oxygen ion conductor which is exposed to gases having different partial pressures of oxygen. Oxygen tends to move from a gas containing a high concentration of oxygen to one of lower concentration. If the two gases are separated from each other by an oxygen ion conductor, the oxygen molecules will dissociate on one surface of the conductor and absorb- electrons to form oxygen ions. These ions can then diffuse through the ionic conductor, leaving the entry surface with a deficiency of electrons. On the exit or low oxygen concentration side of the conductor, oxygen ions leaving the material must give up electrons to form molecular oxygen, leaving the exit surface with an excess of electrons. Thus, an electrical potential difference, or EMF, is set up between' the two surfaces of the ion conductor. The greater the difference in oxygen content of the two gases, the greater will be the tendency of oxygen to diffuse through the conductor, and the greater will be potential difference between the entry and exit surfaces. The EMF generated by the difference in partial pressures may be calculated by the Nernst relation: EMF = t . (RT/nP) ln (P n /P ' ) , (1) 1 υ 2 υ 2 where t. is the ionic transference number, R is the gas constant, T is the absolute temperature, n is the number of electrons involved in the electrode reaction, F is the Farady constant, and P n and υ 2 P' π are the oxygenpartial pressures in the υ 2 first and second gases, respectively. In the present case, the electrode reaction is _2 0 2 + 4e ■ * 20 , and thus n = 4. • A common known oxygen sensor is disclosed in A.M. Chirino and R.T. Sproule, "Application of High and Low Temperature Direct Continuous Oxygen Sensors", 59 Am. Ceramic Soc. Bull. 605 (1980). The oxygen ion conductor material used therein is a solid solution of Zr0 2 and approximately 8% by weight Y 2 °3* The addition of the Y 2°3 to the ZrO- provides vacant oxygen sites in the material which are necessary for diffusion of the oxygen ions. The stabilized Zr0 2 is formed into the shape of a tube closed at one end, the tube typically being approximately 1 cm in diameter with wall thickness of 0.125 cm and 15.0 cm in length. The outer surface of the tube is exposed to the combustion exhaust gases, generally having a low oxygen content. The inner surface is simultaneously exposed to a reference atmosphere, usually atmospheric air, containing a higher oxygen content. Both surfaces of the tube are covered with a porous platinum metal coating which allows the gaseous oxygen to reach the Zr0 2 and provides an electrical contact for measurement of the generated EMF. Calcia-stabilized Zr0 2 tubes have also been constructed, although the yttria-stabilized tubes are preferred due to their higher ionic conductivity and lower activation energy. Similarly, the use of ceria (Ce0 2 ) ceramic tubes has also been studied. There are several disadvantages to the Zr0 2 and Ce0 2 electrolyte tubes. Raw material costs are relatively high, particularly in the case of yttria-stabilized r0 2 . Moreover, very high temperatures are required for the ceramic processing of Zr0 2 and Ce0 2 , which have melting points of 2700°C and 2600°C, respectively. The combination of these two disadvantages results in relatively high tube costs. The long term usefulness of the zirconia-based electrolytes may be lost due to destabilization or the growth of monoclinic grains into the fluorite grains, either of which leads to degraded signal output. Additionally, the geometry of the tube leads to large internal resistances in the sensor requiring that the electrolytes be heated to approximately 600°C to reduce the internal resistance below the external load resistance. Moreover, the entire, platinum-coated outer surface of the electrolyte tube is exposed to the exhaust gas which can result in undesirable corrosion and/or erosion problems; and the relatively small thermal conductivity of the stabilized zirconia can lead to thermal shock problems on thermal cycling, particularly with large tubes. Turning to oxygen separators, the basic principles underlying operation of an oxygen separator stem from the same principles responsible for the functioning of the oxygen sensor, and demonstrate the reciprocity principle of physics. If an oxygen ion conducting material separates two gases with different oxygen partial pressures P n and P' n , then a voltage signal will u 2 u 2 appear across the material due to the diffusion of oxygen ions thereacross. The ions diffuse through the material to equalize the partial pressures, and a basic oxygen sensor is the result. However, if a voltage is applied to the oxygen ion conducting material, and if P n = P' n , the oxygen ions υ 2 u 2 will be forced to flow across the material such that P 3. p 1 . Thus, one gas will become richer in oxygen than the other, resulting in a basic oxygen separator. As an alternative way of viewing the operation of an oxygen separator, consider an oxygen sensor in which a certain voltage signal V is generated by two gases in which P n ≠ U 2 P' n . Now, if a reverse voltage -V is u 2 applied to the material, the flow of oxygen ions through the material will be completely stopped. Increasing the magnitude of the negative voltage will then cause oxygen ions to flow in a reverse direction. Consequently, an oxygen separator can be formed by operating an oxygen sensor in reverse. Disclosure of Invention • The present invention overcomes the disadvantages noted above and provides practical oxygen sensors, fuel cells and oxygen separator generally of the oxygen ion conducting type. The ceramic materials used such devices may be represented by the following formulas: Ni <N bl _ Λ ) 2 0 6 _ χ Ni 2< Nb l-x M x>2°7-x ' where M is selected from the group consisting of Zr +4 , Ti +4 , Sn +4 , Sm +4 , Hf +4 , Ce +4 and mixtures thereof, and where x is a value from 0 to 0.2. Additionally, the ceramic material may be Bi 2 0 3 in solid solution with either Y 0 3 or Nb 2 O s . A preferred electrolytic ceramic material for use in the device is NiNb 2 0 g , which may be produced by mixing Nb 2 0-. and NiO in appropriate amounts. The mixture is then calcined for approximately two hours at 1000°C, and sintered for approximately one hour at 1350 β C. However, all of the above ceramic materials are useful in the practice of the present invention. As used herein, the term "device" includes either an oxygen sensor, a fuel cell or an oxygen separator. Such a device includes at least two layers of a porous metallic conductor. A layer of the ceramic material of the present invention is disposed between the metallic layers to form at least a portion of a solid body for the device. Individual electrodes are connected to each of the metallic layers, and the device is located relative to two gases so that one layer is exposed to a first gas, and the second layer is exposed to a second gas. The porous metallic layers may be made of platinum or other suitable metal. The device may also include a plurality of layers of the electrolytic ceramic material. A plurality of layers of a porous metallic conductor are provided, and each metallic layer is interposed between and contained by two of the ceramic layers to form a solid body of alternating ceramic and metallic layers. The body has first and second opposing sides, and first alternate ones of the metallic layers are exposed along the first side of the body, while second alternate ones of the metallic layers are exposed along the second side. A first electrode connects the first alternate metallic layers, and a second electrode connects the second alternate metallic layers. Accordingly, it is an object of the present invention to provide an oxygen ion conducting device for use as an oxygen sensor, fuel cell or oxygen separator; to provide such a device including a layer of an electrolytic ceramic material between layers of a porous metallic material; to provide such a device having reduced material and production costs relative to presently known types of such devices; to provide such a separator having a high degree of thermal shock resistance; to provide such a device that, when used as an oxygen separator, has a reduced threshold operating temperature; and to provide such a device that is simple and can be made of relatively small size., Other ■ objects and advantages of the invention will be apparent from the following description, the accompanying drawings and the appended claims. .Brief Description of the Drawings Fig. 1 is a perspective view of a multi-layer device according to the present invention, useful as an oxygen sensor, fuel cell or oxygen separator; Fig. 2 is a schematic representation of the device of Fig. 1; Fig. 3 is a graphical representation of the ionic conductivity of NiNb 2 0 fi at several densities and of Zr0 2 + 8% Y 2 °3 as a function of temperature; Fig. 4 is a graphical representation of initial operating temperature of multi-layer devices constructed of NiNb 2 O g at one of several densities as a function of the number of layers of NiNb 2 0 6 ; Fig. 5 is a graphical representation of the ionic conductivity of Bi 2 0 3 :Y 2 0 3 , Bi 2 0 3 : Nb 2 0 5 and Zr0 2 :Y 2 0 3 as a function of temperature; Fig. 6 is a graphical representation of initial operating temperature of multi-layer devices constructed of Bi 2 0 3 :Y 2 0 3 and Bi-0-,:Nb 2 0 5 as a function of the number of ceramic layers in the device; and Fig. 7 is a schematic representation of an exemplary oxygen separator embodiment. Modes for Carrying Out the Invention A preferred oxygen ion conducting ceramic material for use in the practice of the present invention is Ni b 2 o g . It has been found that NiNb 2 0 β can be formed as a dense ceramic body by mixing Nb 2 0 5 and NiO, calcining for 1 to 3 hours at 800°C to 1000°C, preferably two hours at 1000°C, and sintering for 1 to 30 hours at 1200°C to 1400°C, preferably one hour at 1350°C. A ratio of 78.07% b,0 5 to 21.93% NiO by weight is preferred. Under the preferred conditions, the ceramic sinters with no weight loss or gain to a density of 97.2% of 3 the theoretical density of 5.653 gm/cm . A higher percentage of the theoretical density may be achieved using one of several methods well known in the ceramic art including, for example, a longer sintering time, finer starting particle size or hot-pressing. Ionic conductivity measurements made on three bar samples of the NiNb 2 0 g ceramic material at three different densities and on a portion of a densified Zr0 2 plus 8% ^ 2 ° ceramic tube were used to obtain the data shown in Fig. 3. These data are plotted according to the ionic conductivity relation σT=A exp(-Q/kT) (2) where σ is the ionic conductivity, A is a constant, Q is the activation energy, and k is Boltzman's constant. The Fig. 3 data show that the ionic conductivity of Ni b 2 O g increases very rapidly with increasing density and approaches the conductivity of Zr0 2 :Y 2 0 3 . The Fig. 3 data were fitted to the ionic conductivity relation set out as Eq. (2) above, and the resulting fitting parameters are given in Table I. Table I Ionic Conductivity Parameters Material Ln A Q(ev) NiNb 2 O g , 75.4% theo. density 12. 31 1.27 Ni b 2 0 6 , 93.8% theo. density 11.87 1 .28 NiNb 2 O g , 97.1% theo. density 15.38 1.31 Zr0 2 + 8% Y 2 0 3 14. 30 1.03 For Zr0 2 :Y 2 0 3 , the activation energy in Table I and σ- values from Fig. 3 agree well with published data. For NiNb 2 0 g , the Table I data show that the rapid increase in σ with density is primarily due to the rapid increase of In A with density. X-ray analysis of NiNb 2 0 g has shown that the ceramic is a single-phase, columbite structure. Consequently, it is believed that the oxygen ion conductivity is due to the oxygen vacancies in the columbite structure. The columbite structure, AB 2 O g (where A and B are metal cations and 0 is oxygen) , is obtained from the pyrochlore structure, A 2 B 2 0 7 , by the removal of layers of A and 0 ions. In turn, the pyrochlore structure has an eighth layer of oxygen ions missing in comparison to the 4 Og fluorite structure, which has no oxygen vacancies. It will be noted that r0 2 and Ce0 2 have the fluorite structure, and oxygen vacancies for ion conductivity must be produced by dopants such as CaO or Y 2 0 3 . No such dopants are necessary in the case of NiNb 2 O g . Other ceramic materials useful in the practice of the present invention include two families of ceramics, one being the columbite structure exemplified by NiNb 2 0 g , and ' the second being the pyrochlore structure exemplified by i 2 b 2 0 7 . These materials are represented by the following formulas: Ni < Nb l-x M x>2°6-x and N V Nb l-x M x>2°7-x ' +4 +Λ +4 +4 where M may be Zr , Ti , Sn , Sm , Hf or Ce , and where x is a value from 0 to 0.2. It is noted that ionic radii considerations favor Ti +4 , Sm +4 Hf +4 and Zr +4 . Some of these materials may have higher ionic conductivities than NiNb 2 O g . Thermal conductivity measurements performed at room temperature on a sample of the NiNb 2 o g ceramic material at approximately 97% of theoretical density indicate a very large value, 0.036 cal sec cm K~ . By way of comparison, this thermal conductivity is approximately 60% of the alumina value at room temperature which, as is well known, has one of the largest room-temperature thermal conductivities of any known non-metal. The thermal expansion coefficient of the NiNb 2 O g ceramic is 48 X 10 ~7 K~ 1 at room temperature. This moderate thermal expansion coefficient combined with the large thermal conductivity value ensures thermal-shock resistance for this ceramic. Because of the convenient sintering temperatures of the ceramic materials of the present invention (approximately 1350°C) , the ceramics can be "tape cast" into a monolithic body. As is well known in the ceramic art, tape casting is a process for making a multi-layered body (for example, a ceramic capacitor) wherein appropriate metal electrodes are interdispersed between the ceramic layers. A schematic representation of an oxygen sensor (which is a reversed oxygen separator, and vice versa) constructed according to tape-casting methods is shown in Figs. 1 and 2. As seen in Fig. 2, an oxygen sensor 10 is shown mounted through a baffle 12 disposed so as to maintain a first gas having an oxygen partial pressure P_ on the υ 2 second gas having an oxygen partial pressure P' n less than that of the first gas is υ 2 maintained on the side of baffle 12 indicated generally at 16. The sensor 10 includes a body 18 formed of alternating layers 20 of an electrolytic ceramic material and porous layers of a metallic material. Of the metallic layers, alternate layers 22 extend to a first side 24 of body 18 where they are exposed to the first gas at 14. The remaining metallic layers 26 are exposed along a second, opposing side 28 of body 18 to the second gas at 16. An electrode 30 is connected to the metallic layers 22, while an electrode 32 is connected to metallic layers 26. The metallic layers 22 and 26 are preferably of platinum, although they may be constructed of any suitable metallic catalytic metal material. The layers 22 and 26 are fine-grained to avoid irreversible electrode effects, and are sponge-like to permit very rapid oxygen transport within the electrode layers. The oxygen contained within the first and second gases diffuses into the metallic layers as indicated by arrows 34, and thus the oxygen concentration within layers 22 corresponds to the concentration within the first gas, and the oxygen concentration within layers 26 corresponds to that of the second gas. Consequently, the oxygen ion concentrations at any two opposing metallic layers are different, and an EMF is developed by the oxygen ions diffusing across the separated ceramic layers 20. The gaseous oxygen resulting in metallic layers 26 then diffuses into the second gas along the path shown by arrows 36. In essence, therefore, the oxygen sensor 10 consists of N galvanic cells connected in parallel, where N is the number of ceramic layers. The voltage output signal across electrodes 30 and 32 may be calculated through use of the Nernst equation set out above as Eq. (1) . Since an oxygen sensor and an oxygen separator are essentially the same device, the multi-layer geometry described in connection with a sensor may also be used for an oxygen separator. This geometry is preferred for an oxygen sensor, and also represents the best mode presently contemplated for an oxygen separator. In particular, the advantages of such a geometry include ease of construction by a tape-casting technique (to be described in detail below) , and the ability of such a geometry to produce a device that is relatively compact in physical size while presently a substantial surface area of the ceramic material for ion diffusion. It should be recognized, however, that in order to achieve large throughputs, it may turn out that the exposed outer surface area could be sufficiently important that other geometries for the separator may ultimately prove to be more desirable. For example, the separator could be constructed in the form of a tube or manifold. Those skilled in the art will readily recognize that the devices disclosed in the foregoing description are also well-suited for use as fuel cells. Such a device, for use in converting chemical energy produced by oxidation- reduction reactions in which oxygen is involved directly into electrical energy, may be constructed from materials and by methods substantially identical to those described above. Since a fuel cell of this type operates in essentially the same manner as an oxygen sensor, such a device is considered to be well within the scope of the present invention. Due to the temperature dependance of the Nernst relationship, it will be seen that some means for determing the temperature of the device must be provided to control the voltage signal input into the separator properly. This may be accomplished, for example, either by using standard thermocouple methods or by silk-screening a Pt+Pt-20% Rh thermocouple joint directly into the multi-layered device. A multi-layer device is preferably constructed by a tape-casting technique. A powdered electrolytic ceramic material of approximately one micron grain size is mixed with an appropriate organic binder and prepared into a film sheet, preferably of 0.0O75 cm thickness. A platinum layer is silk-screened onto the sheet, and a predetermined number of such sheets are stacked. The stack is heated at 250°C to 400°C for 2 to 30 hours, preferably 290°C for 28 hours, so as to completely burn out the binder material. At the same time, 6 2 pressure of 0 to 1.4 x 10 N/m is applied to the stack to aid in holding it together. The heating of the stack is then increased, preferably at approximately 150°C per hour, to a final temperature of 1200°C to 1400°C (preferably 1320°C) , at which the stack is held for 30 minutes to 3 hours at an applied pressure of 0 to 3.5 x 10 7 N/m2. One major criterion of either an oxygen sensor, fuel cell or oxygen separator is the threshold operating temperature, defined for a sensor as that temperature to which the device must be heated so that the internal resistance of the oxygen sensor is sufficiently below the external load resistance that the sensor output signal can be processed. For Zr0 2 plus 8% Y 2 °3' *~^ e threshold operating temperature is approximately °r For the multi-layer device disclosed herein, the total internal resistance R is R t = R c /N = d/NAα ( 3 ) where R is the resistance of one layer of thickness d and metallic layer area A, σ is the ionic conductivity of the NiNb 2 0 g ceramic, and N is the number of ceramic layers in the device. The threshold operating temperature for the multi-layer NiNb 2 0 g device may be estimated, given that 600°C is the threshold for a Zr0 2 + 8% Y 2 0 3 tube, by solving (R t J Zr0 2 = (R t>NiNb 2 0 6 (4) The typical dimensions of a known zirconia tube oxygen sensor (i. e., approximate diameter of 1 cm, wall thickness of 0.125 cm, and length of 15.0 cm, and the preferred thickness 0.0075 cm and an 2 exemplary surface area 1.6 cm of the disclosed device are used. Additionally, the data of Table I allow estimation of In A and Q as a function of density p by making the reasonable assumption that In A s p and Q <= pfor p >90% of theoretical density. The results of these calculations are shown graphically in Fig. 4 where the temperature is estimated as a function of the number of layers N. Up to the maximum 200 layers shown in Fig. 4 is consistent with state of the art tape casting methods. The graphical representations illustrate that the NiNb 2 O g multi-layer oxygen sensing device can have a significantly lower threshold operating temperature than the presently known zirconia tubes, particularly at higher ceramic densities. It will be noted that these estimates are not particularly sensitive to the tube or multi-layer device dimensions used, and the latter dimensions are intended to be illustrative rather than restrictive. Additionally, any increased ionic conductivity for the device through the use of the alternative materials disclosed herein will result in further lowering of the threshold operating temperature of the device. These concerns are of equal, if not greater importance with an oxygen separator of the type described herein. Since certain threshold operating temperatures exist for various embodiments of the device, it will be necessary to operate the device in a heated environment. Thus, selection of the particular embodiment for the device will depend to some extent upon the availability of such an environment. Another criterion connected with the oxygen sensor is the response time of the device. It is well known that a zirconia tube sensor responds so rapidly (on the order of nanoseconds) that electronic compensation must be employed. The quantity D/d 2 = constant (5) defines the response conditions wherein D is the diffusivity and d is the electrolyte thickness. The condition for the NiNb 2 0 g multi-layer device to respond in the same time as the zirconia tube is α a 2 ) N iNb2θ6 = ( D/d 2 ) Zrθ2 ( 6 ) Employing the Einstein relation. D= (k/N o Z i 2 E 2 ) σT (7) where k is Boltzman's constant, No_ is the density J of mobile ions, Z. is the balance of the ionic species being transported, and e is the electronic charge, connects D and σ . Using the Table I data and Eq. (2), Eq. (6) may be solved for the respective temperatures at which the NiNb- XOO,- multi-layer device and Zr0 2 tube have the same response time. That is, from Eqs. (6) and (7), < D / d2 >NiNb 2 0 6 * < D / d2 >Zr0 2 < 8 > The reduced σ for NiNb 2 O g is compensated for by the reduced d, and it is found that for a ceramic density of 97% of theoretical density, the NiNb 2 O g multi-layer device will actually respond faster than the zirconia tube at all temperatures using the preferred layer thickness. It will be recognized, of course, that while the above calculations concern the NiNb __0 c b multi-layer device, the design and construction techniques of the device may be used with any of the new ceramic materials disclosed herein. In addition, however, it has been found that Bi-0., in solid-solution with either 2 0 3 or Nb 2 0,- has an oxygen conductivity considerably larger than either NiNb 2 0 g or Zr0 2 :Y 2 0 3 . Oxygen conductivity data on these materials similar to that shown in Fig. 3 is presented in Fig. 5. These Bi^O-, ceramics also have sintering temperatures low enough to permit their use with the multi-layer tape casting method described herein. Further, the threshold operating temperatures for devices constructed from these materials, calculated in the a those resented in Fi . 4 ar shown Finally, it will be noted that due to the configuration of the device, the corrosion and/or erosion of the metallic layers in the multi-layer device will be considerably reduced compared to the tube devices. If necessary, however, overcoating of the exposed metallic layers with a protective, porous spinel will maintain the life of the device. Moreover, the relatively small size of the multi-layer device will allow for.the addition of special exhaust-gas filtering and/or purification catalytic devices to protect the sensor. At the same time, the size of the device may be selected so that it is compatible with the fixture geometries currently used with zirconia tubes. The capabilities of an oxygen separator according to the present invention can be better appreciated by considering the exemplary oxygen separator shown in Fig. 7. A single layer separator 40 is mounted into a baffle 42 disposed so as to maintain air on a first side of baffle 42 indicated, generally at 44 and a vacuum on the opposite side indicated generally at 46. The separator 40 includes a body 48 having a layer 50 of an electrolytic ceramic material covered by porous layers 52 of a metallic material. Electrodes 54 are connected to each metallic layer 52, and a voltage source 56 is connected between electrodes 54. Separator 40 may also be exposed on one side (i. e., at 44) to contaminated air or some other gas having an oxygen partial pressure. By driving oxygen ions across layer 50 to fill an evacuated space or enrich the oxygen content of a second gas, a filtration effect can be produced. As indicated in Fig. 7, source 56 applies a voltage V and ceramic layer 50 is of a thickness £ . Assuming that the current I across the ceramic layer 50 is due entirely to movement of oxygen ions (i.e., any electronic conduction is negligible) , the mass m of oxygen transported is m = IMΔt/zeN (5) where M is the molecular weight (16g for oxygen ions), Δt is the time interval in seconds, z is the ionic charge, e is the charge on a single electron, and N is Avogadro's number. Substituting and making the appropriate units conversion. m = (8.29 x 10 "5 )It (6) where m is in grams, I is in amperes and t is in seconds. Substituting from Coulomb's law for I, m =(8.29 x 10 5 )Vt σA/£ (7) where V is the applied voltage, σ • is the ionic conductivity, and A is the exposed area (through porous metallic layers 52) of ceramic layer 50. Taking as an example the Bi 2 0 3 :Nb 2 0 5 ceramic material, the σT data presented in Fig. 6 enables σ to be found as a function of T. For purposes of example, it will be _2 assumed that I = 1.27 x 10 cm, V = 500 volts, and A = 10 3 cm2. Then in one hour the following amounts of oxygen will be passed through ceramic layer 50: Table II Mass of Oxygen Transported T(°C) Mass of Oxygen Transported Per Hour 400 1.572 x 10 4 g = 1572 kg. 500 1.275 x 10 5 g = 12750 kg. 600 6.305 x 10 g = 63050 kg = 0.63 metric tons Thus, in a 24 hour period, the exemplary separator 40 operating at 600°C could transport over 15 metric tons of oxygen into an evacuated space. From a practical point of view, the need to heat an oxygen separator to approximately 500 to 600°C requires such an expenditure of energy that the efficiency of the separator may be a substantial drawback compared to other large scale oxygen separation devices. However, the present invention can be quite useful in applications where efficiency is not as important as convenience, or applications where waste heat is readily available. While the forms of apparatus and the methods herein described constitute preferred embodiments of this invention, it is to be understood that the invention is not limited to these precise forms of apparatus and methods, and that changes may be made therein without departing from the scope of the invention which is defined in the appended claims.

Claims: 1. A device for use as an oxygen sensor in determining the oxygen partial pressure of first gas relative to the oxygen partial pressure of a second gas, comprising: at least two layers (22, 26) of a porous metallic conductor; and at least one layer (20) of an electrolytic ceramic material Ni (Nbi,—X_MX) __0 c o—„ wherein M . is selected from the group consisting of Zr , Ti +4 , Sn +4 , Sm +4 , Hf +4 , Ce +4 and mixtures thereof, and wherein x is from 0 to 0.2; said ceramic layer (20) being disposed between said metallic layers (22, 26) and cooperating therewith to form at least a portion of a body (18) for said device. 2. A device for use as a fuel cell in converting chemical energy into elecrical energy, comprising: at least two layers (22, 26) of a porous metallic conductor; and at least one layer (20) of an electrolytic ceramic material Ni (Nb 1,—XMX) x o 0 c o— wherein M . is selected from the group consisting of Zr , + +4 +4 +4 +4 Ti , Sn , Sm , Hf , Ce and mixtures thereof, and wherein x is from 0 to 0.2; said ceramic layer (20) being disposed between said metallic layers (22, 26) and cooperating therewith to form at least a portion of a body (18) for said device. 3. A device for use as an oxygen separator in separating oxygen from a first gas, comprising: at least two layers (22, 26) of a porous metallic conductor; and at least one layer (20) of an electrolytic ceramic material Ni (Nb ±,— MX) x0O,—X wherein M, . is selected from the group consisting of Zr , +4 +4 +4 4-4 +4 Ti , Sn , Sm , Hf , Ce and mixtures thereof, and wherein x is from 0 to 0.2; said ceramic layer (20) being disposed between said metallic layers (22, 26) and cooperating therewith to form at least a portion of a body (18) for said device. 4. A device for use as an oxygen separator in determining the oxygen partial pressure of a first gas relative to the oxygen partial pressure of a second gas, comprising: at least two layers (22, 26) of a porous metallic conductor; and at least one layer (20) of an electrolytic ceramic material i 2 (Nb, M ) 2 °7_ x wherein M is selected from the group consisting of Zr , +4 4-4 4-4 4-4 4-4 Ti , Sn , Sm , Hf , Ce and mixtures thereof, and wherein x is from 0 to 0.2; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 5. A device for use as a fuel cell in converting chemical energy into electrical energy, comprising: at least two layers (22, 26) of a porous metallic conductor; at least one layer (20) of an electrolytic ceramic material Ni 2 ^ Nb l-x M x^ 2°7-x wnerein M is selected from the group consisting of Zr , Ti +4 , Sn +4 , Sm +4 , Hf +4 , Ce +4 and mixtures thereof, and wherein x is from 0 to 0.2; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 6. A device for use as an oxygen separator for separating oxygen from a first gas, comprising: at least two layers (22, 26) of a porous metallic conductor; at least one layer (20) of an electrolytic ceramic material Ni~ 2.( v Nb1,-xMx)' 2-0-7,-x wherein . M is selected from the group consisting of Zr , 4-4 4-4 4-4 4-4 4-4 Ti , Sn , Sm , Hf , Ce and mixtures thereof, and wherein x is from 0 to 0.2; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 7. A device for use as an oxygen sensor in determining the partial pressure of a first gas relative the oxygen partial pressure of a second gas, comprising: at least two layers (22, 26) of a porous metallic conductor; at least one layer of (20) an electrolytic ceramic, material, said ceramic material being Bi 2 0 3 in solid solution with one member of the group consisting of Y 2 0 3 and b 2 0 5 ; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 8. A device for use as a fuel cell in converting chemical energy into electrical energy, comprising: at least two layers (22, 26) of a porous metallic conductor; at least one layer of (20) an electrolytic ceramic, material, said ceramic material being Bi 2 0 3 in solid solution with one member of the group consisting of 0 3 and Nb 2 0 5 ; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 9. A device for use as an oxygen separator in separating oxygen from a first gas, comprising: at least two layers (22, 26) of a porous metallic conductor; at least one layer of (20) an electrolytic ceramic, material, said ceramic material being Bi 2 0 3 in solid solution with one member of the group consisting of Y 0 3 and Nb 2 0 5 ; said layer (20) of ceramic material being disposed between said layers (22, 26) of said porous metallic conductor and cooperating therewith to form at least a portion of a body (18) for said device. 10. A device as defined by claims 1, 2 or 3 wherein said ceramic material is NiNb 2 O g . 11. A device as claimed by claims 1, 2, 3, 4, 5, 6, 7, 8 or 9, further comprising: a first electrode (30) connected to a first (22) of said layers (22, 26) of said porous metallic conductor; and a second electrode (32) connected to a second (26) of said layers (22, 26) of said porous metallic conductor. 12. A device for use as an oxygen sensor in determining the oxygen partial pressure of a first gas relative to the oxygen partial pressure of a second gas, said first and second gases being maintained in separate relationship, the device comprising: a plurality of layers (20) of an electrolytic ceramic material; a plurality of layers (22, 26) of a porous 0 metallic conductor; each of said layers of porous metallic conductor being interposed between and contained by two of said layers (20) of ceramic material so as to form a solid body (18) of alternating ceramic and 5 metallic layers, said body having first and second opposing sides; first alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said first side of said body (18); o second alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said second side of said body (18) ; a first electrode (30) connecting said first alternate metallic layers (22); and 5 a second electrode (32) connecting said second alternate metallic layers (26); said body (18) being adapted to be disposed such that said first side of said body is exposed to said first gas, and said second side of said body is 0 exposed to said second gas. 13. A device for use as a fuel cell in converting chemical energy released by reaction between a first gas and a second gas into electrical energy, said first and second gases being maintained in separate relationship, the device comprising: a plurality of layers (20) of an electrolytic ceramic material; a plurality of layers (22, 26) of a porous metallic conductor; each of said layers of porous metallic conductor being interposed between and contained by two of said layers (20) of ceramic material so as to form a solid body (18) of alternating ceramic and metallic layers, said body having first and second opposing sides; first alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said first side of said body (18) ; second alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said second side of said body (18) ; a first electrode (30) connecting said first alternate metallic layers (22); and a second electrode (32) connecting said second alternate metallic layers (26) ; said body (18) being adapted to be disposed such that said first side of said body is exposed to said first gas, and said second side of said body is exposed to said second gas. 14. A device for use as an oxygen separator in separating oxygen from a first gas into an area for receiving and holding a second gas, said first gas and said area being maintained in separate relationship, the device comprising: a plurality of layers (20) of an electrolytic ceramic material; a plurality of layers (22, 26) of a porous metallic conductor; each of said layers of porous metallic conductor being interposed between and contained by two of said layers (20) of ceramic material so as to form a solid body (18) of alternating ceramic and metallic layers, said body having first and second opposing sides; first alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said first side of said body (18) ; second alternate ones (22) of said layers (22, 26) of porous metallic conductor being exposed along said second side of said body (18) ; a first electrode (30) connecting said first alternate metallic layers (22); and a second electrode (32) connecting said second alternate metallic layers (26) ; said body (18) being adapted to be disposed such that ' said first side of said body is exposed to said first gas, and said second side of said body is exposed to said area for receiving and holdin a second gas. 15. A device as defined in claims 12, 13 or 14 wherein said ceramic layers (20) are NiNb 2 O g . 16. A device as defined in claims 12, 13 or 14 wherein said ceramic layers (20) are Ni(Nb 1 _ χ M χ ) 2 O χ _ 6/ with M being selected from the group consisting of Zr +4 , Ti +4 , Sn +4 , Sm +4 , Hf +4 , Ce 4 , and mixtures thereof, and x being from 0 to 0.2. 17. A device as defined in claims 12, 13 or 14 wherein said ceramic layers (20) are Ni 2 (Nb l-x M x 2°7-x. with M being selected from the group consisting of Zr +4 . Ti +4 , Sn +4 , Sm +4 , Hf +4 , Ce 4 , and mixtures thereof, and x being from 0 to 0.2. 18. A device as defined in claims 12, 13 or 14 wherein said ceramic layers (20) are Bi 2 0 3 in solid solution with 2 0 3 - 19. A device as claimed in claims 12, 13 or 14 wherein said ceramic layers (20) are Bi 2 0 3 in solid solution with Nb 2 0 t -. 20. A device as defined in claims 1, 2, 3, 4, 5, 6, 7, 8, 9, 12, 13 or 14 wherein said porous metallic conductor is platinum.

Inventors: LAWLESS WILLIAM NICHOLAS, LAWLESS, WILLIAM, NICHOLAS
Applicants: LAWLESS WILLIAM NICHOLAS, LAWLESS, WILLIAM, NICHOLAS
Application year: 1984
Main classification: G01N27
IPC codes: G01N27, H01M8