Superconducting circuit elements with metallic substrate and method for manufacturing the same

Abstract: These superconducting circuit elements, namely SNS heterostructures, such as, e.g. Josephson junctions and field-effect transistors, have a sandwich structure consisting of at least one layer (8) of high-T c superconductor material arranged adjacent to a metallic substrate (9), possibly with an insulating layer (10) in between, the substrate (9), the superconductor (8) and -if present- the insulator (10) all consisting of materials having at least approximately matching molecular structures and lattice constants. Electrical contacts, such as source, drain and gate electrodes (11, 12, 13) are attached to the superconductor layer (8) and to the substrate (9), respectively. The electrically conductive substrate (9) consists of a metallic oxide such as strontium ruthenate Sr₂RuO₄, whereas the superconductor layer (8) is of the copper oxide type and may be YBa₂Cu₃O 7-δ , for example. The insulator layer (10) may consist of SrTiO₃. The manufacture of these devices starts with the preparation of the substrate material from a 2:1,1 molar ratio of SrCO₃ to RuO₂ and involves a floating zone melting process yielding single crystals of the strontium ruthenate Sr₂RuO₄ material onto whose (001) surface the superconductor layer (8) as well as the barrier layer (10) can be epitaxially deposited.

Description: This invention relates to superconducting circuit elements, namely heterostructures, such as, e.g. SNS Josephson junctions and field-effect transistors, having a sandwich structure consisting of at least one layer of high-T c superconductor material arranged adjacent to a metallic substrate, possibly with an insulating layer in between, both the substrate and the insulator consisting of materials having structural properties sufficiently similar to those of the superconductor so that mechanical and chemical compatibility is guaranteed. For device applications of high-T c superconductors, it is desirable to find electrically conductive materials, in particular metals, which are compatible with the high-T c superconductor materials. Compatibility in this context means a best possible match of the respective lattice constants, and the absence of deleterious diffusion effects at the interfaces of the materials involved. These materials may be used, for example, in thin film form for SNS heterostructures (where S stands for superconductor, and N stands for normal metal), or they may serve, e.g., as the bulk substrate in a field-effect transistor. EP-A-0 409 338 discloses a planar Josephson device of the type where at least one layer of non-superconducting material is arranged between two layers of a superconductor material. In one embodiment described, the superconductor is YBa 2 Cu 3 O 7-δ and the non-superconductor is silver sulphate Ag 2 SO 4 , the latter being connected to the superconductor through layers of silver which serve to prevent diffusion of the sulphate into the superconductor. In WO-A-9 004 857 is described an epitaxially deposited Ba-Y-CU-O superconductor film on a crystal substrate, with a close lattice match between substrate and film. The material for the substrate crystal has the K 2 NlF 4 modified perovskite structure. Another example of a substrate with lattice match to a superconductive film is revealed in Applied Physics letters, vol. 53, no. 26, 26 December 1988, pages 2677 - 2679. The used substrate material is LaAlO 3 which is a perovskite like material. The existence of an electrical field-effect in copper oxide high-T c superconductors (although later found to be very small) has already been reported by U. Kabasawa et al. in Japanese Journ. of Appl. Phys. 29 L86, 1990, and EP-A-0 324 044 actually describes a three-terminal field-effect device with a superconducting channel in which electrical fields are used to control the transport properties of channel layers consisting of high-T c superconductor materials. While this seemed to be a promising approach, growth studies of such devices have shown that in the suggested configuration, the ultrathin superconducting layers readily degrade during deposition of insulator layer and top electrode. In EP-A-0 494 580 (Appln. Nr. 91 810 006.6), a field-effect transistor is taught in which the lattice constant matching problem is tackled by using doped and undoped versions of the same material. In casu, the substrate, used as the gate electrode of a field-effect transistor of the MISFET type, consists of conducting niobium-doped strontium titanate. Onto that substrate, a barrier layer consisting of undoped strontium titanate is epitaxially grown, and onto the latter the current channel layer consisting of the superconducting YBa 2 Cu 3 O 7-δ is epitaxially deposited. It has been found (cf. H. Hagesawa et al., Jap. Journ. Appl. Phys., Vol. 28 (1989) L2210) that during film growth a thin insulating surface layer forms on the Nb-doped SrTiO 3 , reducing the sensitivity of the device. The formation of this layer is possibly due to a diffusion of Nb atoms from the gate/insulator interface into the bulk of the gate electrode. Undesired surface layers of this kind can be avoided if substrates are used as gate electrodes which are intrinsically metallic and that do not rely on dopants to induce metallic behavior. It is an object of the present invention to overcome these disadvantages of the prior art. In accordance with the invention, metallic strontium ruthenate (or strontium ruthenium oxide) Sr 2 RuO 4 is used as substrate material for the high-T c superconductor. The existence of Sr 2 RuO 4 , a paramagnetic electrical conductor, is already known from reports by J.J. Randall et al.,"The Preparation of Some Ternary Oxides of the Platinum Metals", J. Am. Chem. Soc. Vol. 81 (1959) pp. 2629-2631, and by A. Callaghan et al., "Magnetic Interactions in Ternary Ruthenium Oxides", Inorganic Chem., Vol. 5, No. 9 (1966) pp. 1572-1576. Of course, at the time of these reports, the high-T c copper oxide superconductor materials were still unknown. Single-crystals of Sr 2 RuO 4 were grown for the first time by the inventors and revealed a highly conductive metallic in-plane behavior which was not before known from the ceramic Sr 2 RuO 4 bulk material. Most of the high-T c superconductor materials known today have very similar molecular structures and essentially the same lattice constants. Examples of high-T c superconductors of the copper oxide type which can be used in connection with the present invention are listed in the table below, together with the respective reference where a description can be found: Superconductor Composition Reference Tl-Ba-Ca-CuO EP-A-0 332 309 Tl-Ba-Ca-Y-CuO EP-A-0 368 210 Bi-Sr-Ca-CuO EP-A-0 332 291 EP-A-0 362 000 EP-A-0 366 510 Bi-Pb-Sr-Ba-CuO EP-A-0 348 896 Bi-Pb-Sr-Ca-CuO EP-A-0 400 666 La-Y-Bi-Sr-CuO EP-A-0 287 810 Eu-Ba-CuO EP-A-0 310 246 Yb-Ba-CuO EP-A-0 310 247 Sr-La-CuO EP-A-0 301 958 In addition to the high-T c copper oxide superconductor materials of which examples are listed above, there are some other high-T c superconductor materials known which do not rely on copper but other elements, such as bismuth, for example. One such material is Ba 0.6 K 0.4 BiO 3 which was described by R.J. Cava et al., "Superconductivity Near 30 K Without Copper: The Ba 0.6 K 0.4 BiO 3 Perovskite", Nature, Vol. 332, No. 6167, pp. 814-816 (1988). The common characteristic of all known high-T c superconductor materials which may be used in connection with the invention is that they have a perovskite or perovskite-related structure. Apparently, of all high-T c superconductor materials known so far, YBa 2 Cu 3 O 7-δ is the one best investigated. This material and methods for its manufacture are, for example, described in the following references: EP-A-0 282 199, EP-A-0 285 168, EP-A-0 286 823, EP-A-0 301 655, EP-A-0 310 248, EP-A-0 311 804, EP-A-0 321 862, EP-A-0 341 788, EP-A-0 349 444, EP-A-0 405 352. Without intending to be restrictive, the description of the invention given below will use YBa 2 Cu 3 O 7-δ (with 0 ≤ δ ≤ 1) as an example of a high-T c superconductor material, with the understanding that any other high-T c superconductor material can be used instead, provided its molecular structure and lattice constants are sufficiently close to those of strontium ruthenate Sr 2 RuO 4 , and this is the case at least with all known high-T c copper oxide superconductors and the bismuth oxide compound mentioned above. In accordance with the present invention, the disadvantages of the prior art are overcome by superconducting circuit elements having a multilayered structure, comprising at least one layer of a high-T c superconductor material arranged adjacent to a substrate consisting of a metallic conductor material having a molecular structure and lattice constants which at least approximately match those of said high-T c superconductor material, the circuit elements being characterized in that said high-T c superconductor material is of the perovskite-related type and that said electrically conductive substrate consists of strontium ruthenate Sr 2 RuO 4 . The method for manufacturing superconducting circuit elements in accordance with the invention is characterized by the following steps: Weighing appropriate ratios of strontium carbonate SrCO 3 and ruthenium dioxide RuO 2 , and grinding; Mixing the powder with water and pressing it to form two rods; Sintering the rods in air at a temperature of about 1300°C; Melting the rods in air in a floating zone melting process; Growing samples from the melt having cylindrical shape with layers (a-b-planes) of strontium ruthenate Sr 2 RuO 4 along the axis of the cylinder; Cleaving the melt-grown samples to obtain single-crystal substrates having defined crystallographic surfaces; Rinsing the substrate in a cleaning solvent; Attaching the single crystal to the heater of a sputtering chamber and sputtering with the following parameters: substrate heater block temperature: 700-750°C; total pressure (Ar/O 2 = 2:1): 84.5 Pa (0,845 mbar); plasma discharge: 150-170 V, 450 mA, aftergrowth cooldown in ≃ 50 kPa (0,5 bar) O 2 lasting for ≃ 1 hour; Epitaxially growing on at least one (001)-surface of the Sr 2 RuO 4 substrate a film of a high-T c superconducting material, with the thickness of the superconductor film being in the range of 1 to 1000 nm; Depositing metal pads onto the superconductor layer(s) to form electrical contacts; Applying a metal pad to the surface of the substrate facing away from said superconducting layer to form an electrical contact. Details of three embodiments of the invention will hereafter be described by way of example and with reference to the drawings in which : Fig. 1 shows the resistivity ρ c -versus-temperature characteristic of Sr 2 RuO 4 ; Fig. 2 is a diagram showing the resistance of a YBa 2 Cu 3 O 7-δ film grown on a Sr 2 RuO 4 substrate in dependence on temperature; Fig. 3 shows an SNS heterostructure with a Sr 2 RuO 4 substrate; Fig. 4 is an inverted MISFET structure using a Sr 2 RuO 4 substrate; Fig. 5 shows essentially the device of Fig. 4 with a supporting layer. A metallic substrate is highly desirable for thin film applications of high-T c superconductor materials, such as, e.g., YBa 2 Cu 3 O 7-δ , for a number of reasons: It can be used as a gate electrode in a field-effect device. It can be used as a shunt resistance. It has a higher thermal conductivity than SrTiO 3 and, therefore, allows denser packaging of the devices. It offers a convenient electrical contact from the superconductor to the external world or to other devices. The problem with the metals and alloys so far considered for use in connection with high-T c superconductor materials is simply that none of them has a lattice that matches the lattice structure of the superconductor material in question to any useful extent. Also, in some cases, diffusion across the interface between the materials tends to destroy the ability to become superconducting. Accordingly, none of these metals has found an application together with a high-T c superconductor, except, perhaps as a contact material. In contrast, the paramagnetic Sr 2 RuO 4 has a layered K 2 NiF 4 -structure and is a metallic conductor along its layers, with an excellent lattice match to copper oxide superconductors, such as YBa 2 Cu 3 O 7-δ . At 300 K, Sr 2 RuO 4 is tetragonal with lattice constants of a = b = 0,387 nm, and c = 1,274 nm, as compared to YBa 2 Cu 3 O 7-δ which is orthorhombic with lattice constants of a = 0,382 nm, b = 0,389 nm, and c = 1,17 nm. This small lattice mismatch (of about 1.3%) compares favorably even to that between YBa 2 Cu 3 O 7-δ (001) and strontium titanate SrTiO 3 {100}, the latter being the standard insulating substrate for the growth of superconducting copper oxides, and which at 300 K is cubic, with a = 0,391 nm (cf. for example, EP-A-0 324 220). Fig. 1 shows the resistivity ρ c -versus-temperature characteristic measured at a representative Sr 2 RuO 4 crystal. No corrections for inhomogeneous current density distribution had to be made. In the a-b-plane, the resistivity ranges from ρ ab ≃10 -4 Ωcm at room temperature down to ρ ab ≃10 -6 Ωcm at 4.2 K demonstrating the highly conductive metallic in-plane behavior of Sr 2 RuO 4 . The observed resistivity along the c-axis resembles that of the layered materials TaS 2 and graphite. Like Sr 2 RuO 4 , they exhibit a metallic behavior along the layers and a resistivity maximum between room temperature and 4,2 K perpendicular to the layers. Generally, when it is possible to grow Sr 2 RuO 4 on SrTiO 3 and vice-versa, thin film devices become feasible where insulating, superconducting and metallic layers can be combined in any way. To demonstrate their compatibility, thin films of YBa 2 Cu 3 O 7-δ were grown onto the a-b-plane of a Sr 2 RuO 4 crystal with very satisfactory results. The diagram of Fig. 2 shows the resistance of such a film in dependence on the temperature, with a critical temperature T c of 86 K. Referring now to Fig. 3, there is shown an SNS heterostructure 1 comprising an electrically conducting Sr 2 RuO 4 crystal forming a substrate 2 and carrying on both sides thin-film superconductor layers 3 and 4 consisting of YBa 2 Cu 3 O 7-δ . As mentioned above, the lattice constants of the substrate material match the lattice constants of the superconductor material to such an extent that epitaxial growth of the superconductor films 3, 4 onto the substrate 2 is possible without a problem. Contact terminals 5 and 6 are attached to superconductor layers 3 and 4, respectively. Fig. 4 shows a field-effect transistor 7 having an inverted MISFET-structure. In this structure, a superconducting YBa 2 Cu 3 O 7-δ film 8 of the thickness s is separated from a Sr 2 RuO 4 crystal substrate 9 serving as a gate electrode, by an insulating SrTiO 3 barrier layer 10 of the thickness t. Besides the thickness s of the superconductor film 8, the resistivity ρ i and the breakthrough field strength E BD of the insulator layer 10 are crucial parameters. The required values for E BD and for ρ i can be simply estimated, if space charge effects are neglected: To induce a surface charge density in superconducting film 8 which corresponds to the unperturbed density n of mobile charge carriers (n ≃ 3...5 × 10 21 / cm 3 , the capacitor formed by substrate 9 and superconductor film 8 has to be biased with a voltage V G = qnst ε 0 ε i where q is the elementary charge, ε ο and ε i are respectively the dielectric constants of the vacuum and of the barrier layer material. Equation (1) rewritten provides the condition for the breakdown field strength E BD : E BD ≥ V g t = q n s ε 0 ε i . Equation (2) implies that to modulate the carrier density n in high-T c superconductors substantially, the product ε i × E BD has to be of the order of 10 8 V/cm. (For comparison, SiO 2 has an ε i × E BD product of 4 × 10 7 V/cm at room temperature.) In addition, the normal-state resistivity ρ i of the insulator has to be sufficiently high to avoid leakage currents which result in an input loss V G × I G , the latter factor being the gate current. For a typical case of I G < I DS /100 and I DS = 10µA, and an area of the substrate 9 of 1mm 2 , the resistivity ρ i must be higher than 10 14 Ωcm/ε i at operating temperature. In view of these requirements, insulating layers with high dielectric constants are recommended. Therefore, and for its good compatibility with the growth of copper oxide superconductors, such as YBa 2 Cu 3 O 7 , SrTiO 3 offers itself as the material for insulating barrier layer 10. The compatibility of YBa 2 Cu 3 O 7 with SrTiO 3 has already been pointed out in EP-A-0 299 870 and EP-A-0 301 646. The dielectric constant ε i of SrTiO 3 being between 40 and 300 (depending on the purity of the material), the breakdown field being on the order of 10 8 V/cm, and with an operating voltage V G = 5V, equation (2) suggests that a monomolecular (i.e. unit cell) layer of superconductor material would meet the requirements. Accordingly, with s = 1,2 nm and ε i = 260 and a carrier density n = 3 × 10 21 cm - 3, equation (1) yields a value of t ≃ 20 nm. The manufacture of the Josephson junction heterostructure of Fig. 3 and of the inverted MISFET device in accordance with Fig. 4 preferably involves the following steps: 1. Appropriate ratios, molar ratios, for example, of strontium carbonate SrCO 3 and ruthenium dioxide RuO 2 are weighed with an accuracy of better than 1 ‰. 2. After grinding, the powder is mixed with water and pressed to form rods of, say, 5 mm diameter, one 10 mm in length, the other 100 mm in length, for example. 3. The rods are sintered on Al 2 O 3 boats in air at about 1300°C. 4. Using the floating zone process, the rods are melted in air in a mirror cavity with focused infrared radiation, the short rod being used as the seed, the long rod being used as the feed material. 5. Single-crystals are grown from the melt. The melt-grown samples have cylindrical shape with layers (a-b-planes) of Sr 2 RuO 4 grown along the axis of the cylinder. The growth of the Sr 2 RuO 4 crystals is complicated by the volatility of RuO 2 which leads to the segregation of SrO. To compensate for this segregation, an excess of RuO 2 must be used in the starting material. A molar ratio of 2:1,1 of SrCO 3 and RuO 2 is recommended to minimize the amount of segregated SrO. In order to grow large crystals, the amount of molten material as well as its composition should be kept constant. This is difficult to achieve probably owing to the continuous evaporation of RuO 2 and because of the low density of the rods. 6. The crystals are then cleaved. Because of the layered structure of Sr 2 RuO 4 , the melt-grown samples can be cleaved easily, and single-crystals may be obtained from the interior part of the cylinder. With this technique it is possible to grow a cylindrical Sr 2 RuO 4 crystal of about 5 mm diameter and 10 mm length. Having prepared the single-crystal Sr 2 RuO 4 substrate, the manufacture of the heterostructure 1 of Fig. 3 involves the following additional steps: 1. The substrate 2 is rinsed in acetone and propanol and attached to the heater of the sputtering chamber with silver paint, for example. 2. On the upper (001) surface of the Sr 2 RuO 4 substrate 2, a superconducting film 3 of, for example, YBa 2 Cu 3 O 7-δ is epitaxially grown by hollow cathode rf-magnetron sputtering, wherein the value of δ is preferably kept equal to zero, but can be made as large as 1. The sputter parameters used encompass a substrate heater block temperature of 700-750°C, a total pressure (Ar/O 2 = 2:1) of 84.5 Pa (0,845 mbar), a plasma discharge of 150-170 V and 450 mA, and an aftergrowth cooldown in ≃ 50 kPa (0,5 bar) O 2 lasting for ≃ 1 hour. The thickness of the superconductor film 3 can finally be in the range of 1 to 1000 nm. 3. The same step is repeated for the lower (001) surface of the Sr 2 RuO 4 substrate 2 to form superconductor layer 4. 4. Electrical contacts are then made in the form of indium dots, silver paint, or metal pads, such as gold pads 5 and 6, for example, on the superconductor layers 3 and 4, respectively. The manufacture of the MISFET-structure 7 of Fig. 4 involves the following steps additional to the preparation of the Sr 2 RuO 4 substrate 9: 1. A {100}-oriented SrTiO 3 barrier layer 10 is epitaxially grown by reactive rf-magnetron sputtering at 6,7 Pa in an O 2 /Ar atmosphere at 650°C (temperature of the sample holder) as an insulator on top of the Sr 2 RuO 4 substrate 9 and is polished down to the desired final thickness. 2. On top of the thinned barrier layer 10, a superconductor film 8 (of YBa 2 Cu 3 O 7-δ , for example) with the thickness s is sputtered. 3. Gold pads 11 and 12 are provided on top of the superconductor layer 8 to form source and drain contacts, respectively. 4. On the back side of the substrate 9, a gate electrode 13 in the form of a metal layer, such as a gold layer, for example, is deposited. 5. Optionally, substrate 9 and gate electrode 13 may be arranged on an insulating support layer 14, be it for stability, as indicated in Fig. 5. Support layer 14 may again consist of SrTiO 3 and be epitaxially grown by reactive rf-magnetron sputtering. The thickness of this layer can be freely chosen. From the measurements taken with several sample embodiments of the field-effect transistor in accordance with Figs. 4 and 5, it has been determined that the operating gate voltage V G should be in the range between 0,1 and 50 V, preferably 5 V, the thickness s of the superconducting film should be in the range between 1 and 30 nm, and the thickness t of the insulating layer should be in the range between 3 and 100 nm. In accordance with the invention, MISFET-type heterostructures consisting of high-T c superconductor/SrTiO 3 /Sr 2 RuO 4 multilayers may be made which allow the application of electrical fields larger than 10 7 V/cm to the superconducting films. In these devices, electric field-effects generate changes in the channel resistance. The high-T c superconductor films have a preferred thickness on the order of 10 nm and are operated with gate voltages well below 30 Volts. The channel resistivity changes can be attributed to equally strong changes of the carrier density in the high-T c superconductor. It should be noted that Sr 2 RuO 4 can also be used in the form of thin films for certain applications. Those skilled in the art will understand that such films can be made with any of the conventional methods, such as electron beam evaporation, thermal evaporation, chemical vapor deposition, metalorganic vapor deposition, laser ablation, rf-magnetron sputtering, spinning-on, molecular beam epitaxy, etc., for example.

Claims: Superconducting circuit element having a multilayered structure, comprising at least one layer (3, 4; 8) of a perovskite/perovskite-related type high-T c superconductor material arranged adjacent to an electrically conductive substrate (2; 9) having a molecular structure and lattice constants which at least approximately match those of said high-T c superconductor material. characterized in that said electrically conductive substrate (2: 7) consists of a metallic conductor material made of strontium ruthenate (Sr 2 RuO 4 ). Superconducting circuit element in accordance with claim 1, characterized in that two high-T c superconducting layers (3. 4) are arranged adjacent said Sr 2 RuO 4 substrate (2) on opposite sides thereof, and that contact pads (5. 6) are attached to said superconducting layers (3, 4), thus forming a Josephson junction. Superconducting circuit element in accordance with claim 1, characterized in that said Sr 2 RuO 4 substrate (2, 9) is a single crystal, and that said at least one superconducting layer (3, 4; 9) is deposited on the {001}-surface(s) of said Sr 2 RuO 4 substrate (2. 8). Superconducting circuit element in accordance with claim 1, characterized in that between said high-T c superconductor layer (8) and said Sr 2 RuO 4 substrate (9) there is arranged a barrier layer (10) consisting of a material whose molecular structure and lattice constants at least approximately match those of the materials of said superconductor layer (8) and of said Sr 2 RuO 4 substrate (9). Superconducting circuit element in accordance with claim 4, characterized in that said barrier layer (10) consists of strontium titanate (SrTiO 3 ). Superconducting circuit element in accordance with claim 4, characterized in that on top of said high-T c superconducting layer (8) first and second contact pads (11, 12) are provided at a mutual distance, forming source and drain electrodes, respectively, and defining a current channel between them inside said superconducting layer (8), and that a third contact pad (13) is attached to said substrate (9) to serve as a gate electrode, thus forming a field-effect transistor. Superconducting circuit element in accordance with any one of claims 1 to 6, characterized in that said high-T c superconductor material consists of YBa 2 Cu 3 O 7-δ , wherein 0 <= δ <= 1. Method for manufacturing superconducting circuit elements in accordance with claim 1, characterized by the following steps: Weighing appropriate ratios of strontium carbonate SrCO 3 and ruthenium dioxide RuO 2 , and grinding; Mixing the powder with water and pressing it to form rods; Sintering the rods in air at a temperature of about 1300ºC; Melting the rods in air in a floating zone melting process; Growing samples from the melt having cylindrical shape with layers (a-b-planes) of strontium ruthenate (Sr 2 RuO 4 ) along the axis of the cylinder; Cleaving the melt-grown sample of Sr 2 RuO 4 to obtain single-crystal substrates (2, 9) having defined crystallographic surfaces; Rinsing the substrate (2, 9) in a cleaning solvent; Attaching the single crystal substrate (2, 9) to the heater of a sputtering chamber and sputtering with the following parameters: substrate heater block temperature: 700-750ºC ; total pressure ( Ar/O 2 = 2 : 1): 84.5 Pa (0,845 mbar); plasma discharge: 150-170 V, 450 mA, aftergrowth cooldown in ∼ 50 kPa (0,5 bar) O 2 lasting for ∼ 1 hour; Epitaxially growing on at least one {001}-surface of the Sr 2 RuO 4 substrate (2, 9) a film (3, 4; 8) of a high-T c superconductor material of the perovskite/perovskite-related type, the thickness of the superconductor film (3, 4; 8) being in the range of 1 to 1000 nm; Depositing metal pads (5, 6; 11, 12) onto said superconductor layers (3, 4; 8) to form electrical contacts; Applying a metal pad (13) to the surface of the substrate (9) facing away from said superconducting layer (8) to form an electrical contact. Method in accordance with claim 8, characterized by the following additional steps: Prior to epitaxially growing said high-T c superconductor layer (8) : Epitaxially growing a {100}-oriented SrTiO 3 barrier layer (10) onto said Sr 2 RuO 4 substrate (9) with the following parameters: Reactive rf-magnetron sputtering at 6,7 Pa in an O 2 /Ar atmosphere; Temperature: approximately 650ºC (temperature of the sample holder); Polishing said SrTiO 3 barrier layer (10) down to a predetermined thickness; On top of the thinned barrier layer (10) continuing with the deposition of the high-T c superconductor layer (8) in accordance with claim 8. Method in accordance with claim 8, characterized by the following additional step: Depositing on the surface of the Sr 2 RuO 4 substrate (9) facing away from said barrier layer (10) an insulating support layer (14) consisting of SrTiO 3 and having a thickness in the range of 100 to 1000 nm. Method in accordance with clairn 8, characterized in that in the starting material for the preparation of the Sr 2 RuO 4 substrate (2, 9) a molar ratio of 2:1 of SrCO 3 to RuO 2 is used. Method in accordance with claim 8, characterized in that in the starting material for the preparation of the Sr 2 RuO 4 substrate (2, 9) an excess of RuO 2 is used to a molar ratio of 2:1,1 of SrCO 3 to RuO 2 . Method in accordance with any one of claims 8 to 12, characterized in that said high-T c superconductor material is YBa 2 Cu 3 O 7-δ , with 0 <= δ <= 1.

Inventors: LICHTENBERG FRANK, MANNHART JOCHEN DR, SCHLOM DARRELL DR, LICHTENBERG, FRANK, MANNHART, JOCHEN, DR., SCHLOM, DARRELL, DR.
Applicants: IBM, INTERNATIONAL BUSINESS MACHINES CORPORATION
Application year: 1991
Main classification: H01L39
IPC codes: C01G55, H01L39, C01G1