FE-CR-AL STAINLESS STEEL HAVING HIGH OXIDATION RESISTANCE AND SPALLING RESISTANCE AND FE-CR-AL STEEL FOIL FOR CATALYST SUBSTRATE OF CATALYTIC CONVERTER

Abstract: A high oxidation resistance Fe-Cr-Al alloy suitable for forming catalytic converter, specifically for forming an auto­ motive catalytic convertes. The alloy is composes: C: less than or equal to 0.02 Wt%; Si: less than or equal to 1.0 Wt%; Cr: in a range greater than or equal to 14 Wt% to less than or equal to 27 Wt%; Al: in a range greater than or equal to 3.5 Wt% to less than or equal to 6.5 Wt%; La: in a range greater than 0.05 Wt% and less than or equal to 0.20 Wt%; Ce: less than or equal to 0.01 Wt%; and remaining being composed of Fe and inevitable impurities.

Description: BACKGROUND OF THE INVENTION Field of the Invention The present invention relates generally to a stainless steel having high oxidation resistance. More specifically, the invention relates to a Fe-Cr-Al alloy having satisfactorily high oxidation resistance and spalling resistance. Further particularly, the invention relates to a Fe-Cr-Al alloy suitable for a catalyst substrate of a catalytic converter. Description of the Background Art In the recent years, atmospheric pollution due to existance of NO x , CO and so forth has become serious environmental problem. Such atmospheric pollution is led by exhaust gas from combustioning facilities, such as internal combustion engines, boilers and so forth. Especially, pollution control has grown as one of the most important tasks to be achieved in automotive vehicle technology. Therefore, it has been become common to provide catalytic converters in exhaust systems of automotive internal combustion engines. As is well known, the catalytic converter generally comprises a catalyst substrate made of a ceramic and catalyst coated on the catalyst substrate surface. The catalyst is held on the catalyst substrate surface by means of catalyst carrier.Conventionally, cordierite (2MgO.2Al₂O₃.5SiO₂) has been utilized as a material for forming the catalyst substrate. In the typical construction, the cordierite catalyst substrate is formed into honeycomb structure by extrusion and baking. γ-alumina fine particles are coated on the surface of the cordierite catalyst substrate to serve as the catalyst carrier. A catalyst made of platinium (Pt) and so forth is bonded on the catalyst carrier. Another catalytic converter has been disclosed in the United States Patent No. 4,331,631, issued on May 25, 1982, to Chapman et al. The disclosure suggests replacing the cordierite catalyst substrate with a metal substrate assembled by an oxidation resistant stainless steel foil into honeycomb structure. By replacing the cordierite catalyst substrate with the thin stainless steel foil catalyst substrate, the wall thickness of the honeycomb structure becomes thinner to expand the open air ratio of honeycomb. As a result, the path area for the exhaust gas can be expanded. Since such catalyst substrate may provide wider path area for the exhaust gas passing therethrough, back pressure of exhaust gas can be reduced and good engine performance can be obtained. In other words, the size of the catalytic converter required for obtaining the desired conversion performance can be reduced by employing a stainless steel foil catalyst base. As is well known, the catalyst carrier is held on the surface of oxide layer formed on metal substrate. It is important that the alloy used as the substrate has good oxidation resistance and spalling resistance. The disclosed invention employs Fe-Cr-Al alloy added an yttrium (Y). In the disclosure, the Fe-Cr-Al alloy is composed of chromium (Cr) of 15 to 25 Wt%, Aluminium (Al) of 3 to 6 Wt% and Y of 0.3 to 1.0 Wt%. Y is indeed rare and expensive material. Furthermore, Y cannot be supplied in sufficient amounts for utilization by the automotive industry to manufacture catalytic converters. On the other hand, the United States Patent 4,414,023, issued to Aggen et al. on November 8, 1983, discloses a Fe-Cr-Al alloy composed of Cr of 8 to 25 Wt%, Al of 3 to 8 Wt%, and an addition of at least 0.02 Wt% and upto 0.05 Wt% from the group consisting of cerium (Ce), lanthanum (La), neodymium (Nd), praseodyminium (Pr) with a total of rare earth metal (REM) upto 0.06 Wt%. This alloy will be hereafter referred to as ''Fe-Cr-Al-REM alloy''. In this Fe-Cr-Al-REM alloy, REM improves the adherence of oxide layer. Such alloy has been conventionally used for electric resistance heating elements. The Fe-Cr-Al-REM alloy has reasonably high oxidation resistance when it is used in the form of a relatively thick plate. However, when it is used as a catalyst substrate, the foil has to be thin enough to provide sufficient path area in view of the engine performance as set forth above. If the temperature of the exhaust gas rises when substantially high load is continuously applied to the engine in high speed crusing, or a spark ignition timing is retarded excessively, rapid oxidation of the overall structure of the alloy occurs and the substrate becomes weak, brittle and easily broken. In addition, as is also well known, pulsatile flow of the exhaust gas tends to be generated during engine driving to cause vibration simultaneously with high temperature oxidation. This tends to cause releasing of the oxide scale from the associated surface of the catalyst substrate. As set forth above, since the catalyst is bonded on the oxide scale by means of the catalyst carrier, the releasing of the oxide scale leads to removal of the catalyst to lower exhaust gas purification performance of the catalytic converter. It should be noted that, through out the following disclosure, the word spalling resistance is used to represent a property of good adherence of the oxide scale on the surface of the catalyst substrate. SUMMARY OF THE INVENTION Therefore, it is an object of the invention to provide an Fe-Cr-Al alloy which has substantially high oxidation resistance and allows good adherence of scale formed on its surface at any environmental condition. Another object of the invention is to provide an Fe-Cr-Al alloy which is suitable to use for forming a catalyst substrate for a catalytic converter for an exhaust system in an automotive engine, a boiler, combustioning systems, and so forth. A further object of the invention is to provide a substantially thin foil of Fe-Cr-Al stainless steel which has sufficient oxidation resistance and spalling resistance for use as the material for forming a catalyst substrate. In order to accomplish the aforementioned and other objects, a Fe-Cr-Al alloy, according to the present invention, comprises: C: less than or equal to 0.02 Wt%; Si: less than or equal to 1.0 Wt%; Cr: in a range greater than or equal to 14 Wt% to less than or equal to 27 Wt%; Al: in a range greater than or equal to 3.5 Wt% to less than or equal to 6.5 Wt%; La: in a range greater than 0.05 Wt% and less than or equal to 0.20 Wt%; Ce: less than or equal to 0.01 Wt%; and the remainder being Fe and inevitable impurities. Optionally Ti and/or lanthanides other than La or Ce can be present as defined in claim 1. Preferred embodiments of the invention are given in the dependent claims. It has found that Ce accelerates oxidation at high temperature and La, Nd and so forth decelerate oxidation to expand the life of the Fe-Cr-Al stainless steel foil in high temperature oxidation. Therefore, by reducing content of Ce, shortening of the life of foil can be avoided. In addition, by including La, Nd and so forth in sufficient quantities, oxidation resistance of the Fe-Cr-Al alloy can be improved. If necessary titanium (Ti) can be added to the aforementioned Fe-Cr-Al alloy in a content range of 5-times or more of content of C and less than or equal to 0.10 Wt%. In the alternative, the Fe-Cr-Al alloy set forth above comprises less than 0.02 Wt%, of La and lanthanide excluding Ce and La in a content greater than or equal to 0.001 Wt% and less than 0.03 Wt%, and total content of lanthanide including Ce and La is less than or equal to 0.20 Wt%. For the latter defined alloy, Ti can be added in a content range of 5-times or more of content of C and less than or equal to 0.10 Wt%. In order to be used as a material for catalyst substrate, the aforementioned alloys may be formed into a thin foil having a thickness in a range greater than or equal to 20 µm and less than or equal to 80 µm. As set forth, La has characteristics which expand the life of stainless steel foil in high temperature oxidation. The alloy is formed into a foil of the thickness in a range of 20 µm to 80 µm, the life of the stainless steel foil becomes insufficient for utilization as a catalyst substrate when the content of La is less than or equal to 0.05 Wt%. In other words, in order to provide sufficient oxidation resistance and spalling resistance, more than 0.05 Wt% of La has to be contained in the alloy forming the catalyst substrate. On the other hand, La has a tendency to degrade hot warkability of the alloy. When the content of La exceeds 0.20 Wt%, it becomes impossible to hot roll the alloy. Lanthanide except for Ce has similar characteristics as set forth above with respect to La. Therefore, in cases lanthanide other than Ce is utilized in the aforementioned Fe-Cr-Al alloy, the overall content should not exceed 0.20 Wt%. In practice, the process for extracting La from the ore becomes easier and simpler if La is extracted with another lanthanide such as Nd. For this reason, it would be practically beneficial to allow inclusion of lanthanide other than Ce and La in a rate greater than or equal to 0.001 Wt% to less than 0.03 Wt%. On the other hand, since Ce accelerates oxidation of the stainless steel foil and shortens the life, content of Ce has to be minimized. Therefore, in order to form the proposed Fe-Cr-Al alloy, Mischmetal which contains 45% to 55% of Ce, 22% to 30% of La and 15% to 18% of Nd, cannot be used. Therefore, a metal which is prepared by removing Ce from Mischmetal, should be used for making the aforementioned Fe-Cr-Al alloy. When the content of Cr is less than 14 Wt%, enough oxidation resistance of the alloy cannot be obtained. Therefore, the content of Cr has to be greater than or equal to 14 Wt%. On the other hand, if the alloy contains Cr in quantities higher than 27 Wt%, it decreases toughness of the alloy and makes it impossible to cold roll the alloy. Therefore, the content of Cr should not exceed 27 Wt%. Similarly, when the content of Al is smaller than 3.5 Wt%, sufficient oxidation resistance cannot be obtained. Therefore, content of Al should be greater than or equal to 3.5 Wt%. On the other hand, when the content of Al is greater than 6.5 Wt%, it is difficult to hot roll the alloy. Therefore, the content should be limited to a range from 3.5 Wt% to 6.5 Wt% inclusive. When the content of Si is greater than 1.0 Wt%, it decreases cold-workability. Therefore, the Si content should not be more than 1.0 Wt%. When the alloy is formed into a plate with relatively large thickness, Si will serve to enhance oxidation resistance. However, when the alloy is formed into substantially thin foil, such as that having a thickness of 20 µm to 80 µm, Si accelerates oxidation to shorten the life of the stainless steel foil in high temperature oxidation. Therefore, it is preferred to limit the content of Si to less than or equal to 0.4 Wt%. C decreases toughness of the alloy and makes cold rolling and other treatment of the alloy difficult. For this reason, the content of C is limited to less than or equal to 0.02 Wt%. As set forth above, Ti can be added to the Fe-Cr-Al alloy composed of the foregoing material. Ti is to be added for improving malleability of the alloy by fixing C. In order to achieve the desired effect, Ti has to be added at an amount of at least 5-times of the amount of C. On the other hand, Ti tends to degrade oxidation resistance of the alloy when it is added in excess of 0.1 Wt%. Therefore, the amount of Ti is limited in a range of 5-times of the weight ratio of C or equal to but not greater than 0.10 Wt%. As is well known, in the stainless steel production process, about 0.02 Wt% of P and about 0.005 Wt% of S are maintained. These serve as inevitable impurities to be contained in the alloy with Fe. However, presence of P and S will not affect the properties, characteristics and productivity of the inventive alloy. On the other hand, N as inevitable impurity serves to decrease toughness similarly to C. Therefore, it is preferable to minimize the content of N. As along as the content of N is maintained less than or equal to 0.02 Wt%, the presence of N will never affect the properties of the stailess steel foil. When the catalyst substrate of honeycomb structure is formed of the Fe-Cr-Al alloy set forth above, it is preferable to minimize the thickness of the stainless steel foil from the viewpoint of the performance of the exhaust system. Namely, by minimizing the thickness of the stainless steel foil, the path area of the honeycomb structure can be maximized to reduce resistance against the flow of the exhaust gas. As will be clear, decreasing of flow resistance for the exhaust gas improves engine performance and fuel economy. In view of the above, it is preferred to provide thickness of the stainless steel foil less than or equal to 80 µm. On the other hand, as will be appreciated, thinner foil will have lower oxidation resistance and thus have shorter life. For this reason, it is not practical to use the stainless steel foil having a thickness less than 20 µm. Therefore, the thickness of the stainless steel foil is practically limited in a range less than or equal to 80 µm and greater than or equal to 20 µm. The Fe-Cr-Al alloy has high oxidation resistance suitable for utilization as catalyst substrate in a catalytic converter for exhaust gas purification and/or applications requiring high adherance of catalyst to its surface. The Fe-Cr-Al alloy set forth above has sufficient malleability to form substantially thin foil having thickness in a range of 20 µm to 80 µm. The present invention is further directed to a stainless steel foil for forming a calalytic converter, which is composed of a Fe-Cr-Al alloy at least comprising Fe, C, Cr, Al, La and inevitable impurities, in which C, Cr, Al and La are present in the following ranges: C: less than or equal to 0.02 Wt%; Cr: in a range of greater than or equal to 14 Wt% and less than or equal to 27 Wt%; Al: in a range of greater than or equal to 3.5 Wt% and less than or equal to 6.5 Wt%; La: in a range of greater than 0.05 Wt% and less than or equal to 0.20 Wt %. The thin foil has high oxidation resistance ability suitable for utilization as catalyst substrate for a catalytic converter for an exhaust gas purification and allows high adherance of catalyst to its surface. The thin foil is formed with thickness in a range of 20 µm to 80 µm. BRIEF DESCRIPTION OF THE DRAWINGS The present invention will be understood more fully from the detailed description given herebelow and from the accompanying drawings of the preferred embodiment of the invention, which, however, should not be taken to limit the invention to the specific embodiment but are for explanation and understanding only. In the drawings: Fig. 1 is a graph showing the result of Charpy test performed with respect to plate formed by hot rolling and annealing treatment; Fig. 2 is a graph showing the result of oxidation test performed with respect to Fe-Cr-Al alloy; Fig. 3 is a scanning electron micrograph of the surface of the inventive Fe-Cr-Al alloy after cyclic oxidation; and Fig. 4 is a scanning electron micrograph of the surface of the comparative example after cyclic oxidation. DESCRIPTION OP THE PREFERRED EMBODIMENT In the preferred embodiments, Fe-Cr-Al alloys are prepared of the materials, i.e. C, Si, Cr, Al, Ti, and REM as shown in the appended table 1. In order to compare the properties of the Fe-Cr-Al alloys constituting the preferred embodiment of the present invention, comparative examples are also prepared of the contents as shown in the appended table 2. It should be noted, in the comparative examples, mischmetal is added for the examples B-2 and B-3. For the remainder, pure rare earth metal or metals are added. In the preparation of samples for testing, at first 10 kg ingots are cast of respective alloys, i.e. A-1 through A-9 and B-1 through B-14. After forming ingots, hot rolling is performed for respective samples to form plates of 3 mm thick at 1200 o C of temperature. During this hot rolling process, the sample B-3 having an REM content of 0.058 Wt%, the sample B-4 having an La content of 0.22 Wt%, the sample B-6 having a Ce content of 0.085 Wt% and the sample B-10 having an Al content of 8.2 Wt% were broken or cracked during rolling process. Therefore, for these samples, i.e. B-3, B-4, B-6 and B-10, the succeding tests were not performed. The remaining samples were annealed at a temperature of 900 o C. Then, Charpy testing was performed with respect to each sample for checking the toughness. The result of Charpy testing is shown in Fig. 1. In the observation of the results of testing, sample A-1 having a C content of 0.001 Wt% and A-3 having a C content of 0.016 Wt% with 0.09 Wt% of Ti added, had a ductile/brittle transition temperature in a temperature range of 50 o C to 70 o C and thus were easily cold rolled. Contrary to this, the sample B-8 having a C content of 0.022 Wt% had a transition temperature of 130 o C, therefore, it was difficult to cold roll. The sample B-8 was therefore processed by warm rolling. Similarly, the sample B-11 containing 27.2 Wt% of Cr and the sample B-14 containing 1.8 Wt% of Si had transition temperatures higher than 100 o C. Therefore, it was impossible to cold roll the samples B-11 and B-14. The samples thus formed into 3 mm thick plates had the scale removed therefrom. It should noted that, since it was not possible to form samples B-8, B-11 and B-14 into 3 mm thick plates, these samples were warm rolled at a temperature lower than 200 o C. The samples formed into 3 mm thick plates were subsequently annealed. By repreating the foregoing process, 50 µm thick and 0.5 mm thick samples were formed. From the foil thus formed, test pieces of 50 µm and 0.5 mm thick, 20 mm width and 30 mm length were prepared. Oxidation testing was performed with respect to each test foil in the atmospher at 1150 o C. The result of the oxidation test thus performed is illustrated in Fig. 2. As will be seen from the tables 1 and 2, the samples A-1 and B-7 have same contents of Cr (20 Wt%) and Al (5 Wt%). 0.08 Wt% of La was contained in the sample A-1 and 0.06 Wt% of Ce was contained in the sample B-7. When the oxidation tests were performed with respect to 0.5 mm thick test pieces of the samples A-1 and B-7, no significant differences between these samples could be found even after 240 hours. However, when the same oxidation test was performed with respect to the 50 µm thick test foils of the samples A-1 and B-7, the gain of weight due to increasing of oxide in the sample B-7 reached 1.0 mg/cm² after about 96 hours, and this quickly increased rate becoming 8.0 mg/cm² after about 120 to 144 hours from the begining of the test. The gain of weight due to oxidation will be hereafter referred to as ''oxidation weight-gain''. In this condition, the test piece of the sample B-7 was completely oxidized and broken into small pieces. On the other hand, the oxidation weight-gain after 240 hours for the test piece of the sample A-1 was 1.1 mg/cm². This is evidence that the sample A-1 has equivalent oxidation resistance to that of the sample B-1 which contains Y. As is well known, Al in the Fe-Cr-Al alloy is oxidized during high temperature oxidation to form Al₂O₃ layer on the surface. This layer serves as the protective layer so as not to oxidize Fe and Cr in the alloy. Therefore, by the presence of Al₂O₃ layer, the Fe-Cr-Al alloy generally has high oxidation resistance. However, in case that the Fe-Cr-Al alloy is formed into thin foil, such as 50 µm thick foil, all Al is oxidized when oxidation period extends for a long period. After all of Al is oxidized, the general effect of the Al₂O₃ layer as described above becomes inapplicable in some alloys. Namely, whether the Al₂O₃ layer is effective or not is determined depending upon the REM contained in the alloy. For example, considering the 50 µm thick foil containing 5 Wt% of Al, the content of Al becomes approximately zero when the oxidation weight-gain reaches 1.0 mg/cm². On the other hand, it should be appreciated that when the same oxidation occurs on a plate of 0.5 mm thick, the content of Al drops from 5 Wt% to 4.5 Wt%. If the alloy contains Ce, oxidation resistance is then lost. Therefore, Fe and Cr in the alloy are quickly oxidized and broken down. On the other hand, if the alloy contains sufficient concentration of La, Nd or Y, oxidation stops when overall Al is oxidized. Therefore, such alloy has substantially long life even when subjected to high temperature oxidation. As will be clear herefrom, La and Nd may provide equivalent effect in expanding the life of such alloys. As will be seen from the table 2, though the comparative sample B-9 contains 0.21 Wt% of Ti, the sample B-12 contains 3.2 Wt% of Al and the sample B-13 contains 13.7 Wt% of Cr, the lives thereof were insufficient. Utilizing the same size test piece as used in the oxidation test, the oxide scale holding ability was tested. In the test, an oxidation cycle, in which oxidation for the test pieces is performed for 30 minutes in an atmosphere of 1150 o C and thereafter rapid cooling of the test pieces is performed for 12 minutes, is repeated for 200 cycles. After 200 cycles of oxidation, the surface condition of respective test pieces is checked by means of a scanning electron microscope. Fig. 3 shows the surface condition of the test piece made of the sample A-2 after 200 oxidation cycles, Similarly, Fig. 4 shows the surface condition of the test piece of the comparative sample B-2. As will be seen from Fig. 3, the oxide scale of the test piece of the sample A-2 could be completely retained. On the other hand, as seen from Fig. 4 approximately half of the oxidation scale on the test piece of the sample B-2 was removed or released from the surface. Similar results were observed on the surface of the test piece of the sample B-5. It should be appreciated that the judgement of the results of the foregoing tests are made according to the following standard. HOT ROLLING ABILITY O: hot rolling was possible after heating at 1200 o C; : hot rolling was not possible after heating at 1200 o C. COLD ROLLING ABILITY O: hot rolled and anealed sample has ductile/brittle transistion temperature lower than 100 o C; : hot rolled and annealed sample has ductile/brittle transition temperature higher than or equal to 100 o C. OXIDATION RESISTANCE O: gain of weight in the 50 µm thick foil after heating at 1150 o C for 168 hours is less than 1.5 mg/cm²; : gain of weight in the 50 µm thick foil after heating at 1150 o C for 168 hours, is greater than or equal to 1.5 mg/cm². SPALLING RESISTANCE O: after 200 oxidation cycles, in each cycle of which the 50 µm thick foil is heated in an 1150 o C atmosphere for 30 minutes and thereafter rapidly cooled for 12 minutes, no release of oxide scale is observed; ; after 200 oxidation cycles, release of oxide scale is observed. EMBODIMENT 2 Respectively 5 ton alloys C-1 and C-2 of the appended table 3 were melted by means of a vacuum melting furnace and cast. Obtained ingots were treated according to the usual process of ferritic stainless steel treating, in which the block is treated through ingot break down step, hot rolling step and cold rolling step to be formed into 0.3 mm thick cold rolled coil. This cold rolled coil was passed through a Senzimir mill to obtain foil coil of 1000 mm width and 50 µm thickness. The cold rolled coil is also passed through a CBS mill to form 30 µm thick foil. In the compositions shown in the table 3, both alloys C-1 and C-2 exibited good hot workability. In the foregoing U. S. Patent No. 4,331,631, it is suggested to perform heat treatment to the surface of the alloy to form Al₂O₃ whiskers. In the disclosed structure, catalyst is coated on the alloy surface with such whiskers. Same treatment was made on the alloy composed according to the invention. After the heat treatment according to the disclosure of the aforementioned U. S. Patent Application, good Al₂O₃ whiskers could be formed.

Claims: An Fe-Cr-Al stainless steel foil consisting of C: less than or equal to 0.02 Wt%; Si: less than or equal to 1.0 Wt%; Cr: in a range of greater than or equal to 14 Wt% and less than or equal to 27 Wt%; Al: in a range of greater than or equal to 3.5 Wt% and less than or equal to 6.5. Wt%; La: in a range of greater than 0.05 Wt% and less than or equal to 0.20 Wt%; and Ce: less than or equal to 0.01 Wt% optionally Ti in a content greater than or equal to 5-times of content of C and less than or equal to 0.10 Wt% and optionally lanthanide other than La and Ce in a content greater than or equal to 0.001 Wt% and less than 0.03 Wt%, and the overall content of the lanthanide including La and Ce being less than or equal to 0.20 Wt%, the remainder being Fe and inevitable impurities. An Fe-Cr-Al stainless steel foil as set forth in claim 1, which has high oxidation resistance suitable for use as catalyst substrate of a catalytic converter for an exhaust gas purification. An Fe-Cr-Al stainless steel foil as set forth in claim 2, which forms a thin foil with thickness in a range of 20 µm to 80 µm. An Fe-Cr-Al stainless steel foil as set forth in claim 1, which further includes Ti in a content greater than or equal to 5-times the content of C, the total amount of Ti being less than or equal to 0.10 Wt%. An Fe-Cr-Al stainless steel foil as set forth in claim 4, which has high oxidation resistance suitable for use as catalyst substrate of a catalyst substrate of a catalytic converter for an exhaust gas purification. An Fe-Cr-Al stainless steel foil as set forth in claim 5, which forms a thin foil with thickness in a range of 20 µm to 80 µm. An Fe-Cr-Al stainless steel foil as set forth in claim 1, which further includes lanthanide other than La and Ce in content greater than or equal to 0.001 Wt% and less than 0.03 Wt%, and wherein overall content of the lanthanide including La and Ce is less than or equal to 0.20 Wt%. An Fe-Cr-Al stainless steel foil as set forth in claim 7, which has high oxidation resistance suitable for use as catalyst substrate of a catalytic converter for an exhaust gas purification. An Fe-Cr-Al stainless steel foil as set forth in claim 8, which forms a thin foil with thickness in a range of 20 µm to 80 µm. An Fe-Cr-Al stainless steel foil as set forth in claim 7, which further includes Ti in a content greater than or equal to 5-times the content of C, the total amount of Ti being less than or equal to 0.10 Wt%. An Fe-Cr-Al stainless steel foil as set forth in claim 10, which has high oxidation resistance suitable for use as catalyst substrate of a catalytic converter for an exhaust gas purification. An Fe-Cr-Al stainless steel foil as set forth in claim 11, which forms a thin foil with thickness in a range of 20 µm to 80 µm.

Inventors: ISHII, KAZUHIDE C/O TECHNICAL RESEARCH DIVISION, KAWASAKI, TATSUO C/O TECHNICAL RESEARCH DIVISION
Applicants: KAWASAKI STEEL CORPORATION
Application year: 1987
Main classification: C22C38
IPC codes: C22C38, F01N3