EP0236823B1 - Metallic semi-finished product, process for its manufacture and uses of the semi-finished product - Google Patents
Metallic semi-finished product, process for its manufacture and uses of the semi-finished product Download PDFInfo
- Publication number
- EP0236823B1 EP0236823B1 EP87102472A EP87102472A EP0236823B1 EP 0236823 B1 EP0236823 B1 EP 0236823B1 EP 87102472 A EP87102472 A EP 87102472A EP 87102472 A EP87102472 A EP 87102472A EP 0236823 B1 EP0236823 B1 EP 0236823B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- semi
- finished product
- process according
- temperature
- annealing
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- 239000011265 semifinished product Substances 0.000 title claims abstract description 22
- 238000000034 method Methods 0.000 title claims description 16
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000013078 crystal Substances 0.000 claims abstract description 23
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 11
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 239000011651 chromium Substances 0.000 claims abstract description 7
- 229910000423 chromium oxide Inorganic materials 0.000 claims abstract description 7
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 claims abstract description 6
- 239000010941 cobalt Substances 0.000 claims abstract description 6
- 229910017052 cobalt Inorganic materials 0.000 claims abstract description 6
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052751 metal Inorganic materials 0.000 claims description 25
- 239000002184 metal Substances 0.000 claims description 25
- 238000000137 annealing Methods 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 7
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 6
- 229910052746 lanthanum Inorganic materials 0.000 claims description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 5
- 229910052760 oxygen Inorganic materials 0.000 claims description 5
- 239000001301 oxygen Substances 0.000 claims description 5
- 239000000047 product Substances 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 229910052772 Samarium Inorganic materials 0.000 claims description 4
- 229910052776 Thorium Inorganic materials 0.000 claims description 4
- 229910052770 Uranium Inorganic materials 0.000 claims description 4
- 229910052791 calcium Inorganic materials 0.000 claims description 4
- 239000003054 catalyst Substances 0.000 claims description 4
- 239000007789 gas Substances 0.000 claims description 4
- 229910052735 hafnium Inorganic materials 0.000 claims description 4
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052727 yttrium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 239000000853 adhesive Substances 0.000 claims description 3
- 230000001070 adhesive effect Effects 0.000 claims description 3
- 238000005524 ceramic coating Methods 0.000 claims description 2
- 229910000531 Co alloy Inorganic materials 0.000 claims 2
- 229910000990 Ni alloy Inorganic materials 0.000 claims 2
- 239000004411 aluminium Substances 0.000 claims 2
- 238000005266 casting Methods 0.000 claims 1
- 238000009749 continuous casting Methods 0.000 claims 1
- 239000011261 inert gas Substances 0.000 claims 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 abstract description 8
- 229910052761 rare earth metal Inorganic materials 0.000 abstract description 5
- 150000002910 rare earth metals Chemical class 0.000 abstract description 5
- 239000010410 layer Substances 0.000 description 17
- 229910045601 alloy Inorganic materials 0.000 description 13
- 239000000956 alloy Substances 0.000 description 13
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910000831 Steel Inorganic materials 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 229910002092 carbon dioxide Inorganic materials 0.000 description 3
- 239000000919 ceramic Substances 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910052684 Cerium Inorganic materials 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- -1 Y2O3 Chemical class 0.000 description 2
- 239000013543 active substance Substances 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000003921 oil Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000007750 plasma spraying Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- 238000007669 thermal treatment Methods 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 239000000443 aerosol Substances 0.000 description 1
- 244000052616 bacterial pathogen Species 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 230000003197 catalytic effect Effects 0.000 description 1
- 239000010724 circulating oil Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000000567 combustion gas Substances 0.000 description 1
- 239000004020 conductor Substances 0.000 description 1
- 239000000356 contaminant Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000001351 cycling effect Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000001784 detoxification Methods 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000010285 flame spraying Methods 0.000 description 1
- 239000011888 foil Substances 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011572 manganese Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000010970 precious metal Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000004071 soot Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 230000004222 uncontrolled growth Effects 0.000 description 1
- 238000010308 vacuum induction melting process Methods 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
Definitions
- the invention relates to a method for producing semi-finished metal products in the form of wire, rods, billets, tubes, in particular sheet metal or strips, for applications in which a high thermal shock resistance and large surface area and / or chemical resistance and / or low thermal conductivity of the surface layer is required , in particular for catalyst supports, soot filters, heating conductors, aerosol filters, linings of chemical and energy converting systems.
- the semi-finished product is based on iron and / or nickel and / or cobalt with 2 to 16% aluminum, 12 to 30% chromium and up to 4% of at least one highly reactive element from the group Y, Zr, Ti, Ce, Sm, Hf , La, Th, U, V, W, Nb, Mo, Gd, Si, Mg, Ca and / or their dispersed oxides.
- An alloy from this area was made from J. Electrochem. Soc., Solid-State Science Technology, Volume 131, No. 4, pages 923-931. By annealing strips of this alloy at temperatures above 1000 ° C in oxygen, oxide-containing surfaces can be created.
- a ferritic stainless steel which can be processed hot and is resistant to temperature changes, oxidation and scaling at elevated temperatures.
- the iron-chromium-aluminum alloy contains cerium, lanthanum and other rare earth metals and is suitable for forming a textured aluminum oxide film on the surface.
- the alloy is produced in the usual way by melting.
- the typical steel impurities such as oxygen, nitrogen and sulfur are reduced before the rare earth metals are added to the melt.
- Any conventional process, including arc furnaces, AOD and vacuum induction melting processes, is applicable.
- the melt is poured into blocks, bars, strips or sheets.
- the steel is then hot and / or cold rolled and subjected to the usual procedures such as descaling and annealing.
- the ferritic stainless steel is then heat treated to form an alumina surface.
- the object of the invention is to provide a semi-finished metal product which, preferably without an intermediate layer (wash coat), represents a temperature change-resistant adhesive base for a catalytically active coating.
- the task also includes the creation of a method which leads in the simplest possible way to a metallic semi-finished product with the property mentioned.
- Form contained gas, in particular CO2 is set under reducing conditions and then in the temperature range from 800 to 1000 ° C for up to 25 h in air, at least in the surface area of Semi-finished metal stem crystals are formed,
- Normal steel contaminants are carbon, nitrogen, oxygen, phosphorus, sulfur, manganese, copper and nickel.
- the surface structure can be clearly seen from the attached micrographs.
- Figure 1 shows a semi-finished product surface produced using conventional methods with irregularly lying whisker-like oxidic stem crystals.
- Figure 2 shows the semi-finished product surface as it is formed when the method according to the invention is carried out.
- the large areas are the metal stem crystals, from the surface of which the oxidic stem crystals have grown like hair.
- Figure 3 shows the oxide stem crystals in 10 times magnification compared to Figure 2. According to this, the axes of the oxide stem crystals are predominantly perpendicular to the geometric surface of the semi-finished product, which is formed by the surfaces of the metal stem crystals.
- the invention provides a semi-finished metal product in which metal stem crystallites are formed at least in the surface area by the directional solidification of the metal alloy. Due to the high cooling rate and thermal treatment, the additional elements from the aforementioned group X, which are highly reactive, i.e. are highly oxygen-affine, or their oxides, which are present in finely divided form in the surface area, in the subsequent heat treatment as germs. At the same time, as a kind of dowel, they ensure a high level of adhesive strength for the thermally grown oxidic stem crystallites. A further improved nucleation is achieved by briefly heating as the first thermal treatment stage under reducing conditions or those that occur during this treatment.
- the long-term annealing treatment under oxidizing conditions, preferably in air, in which the oxidic stem crystallites grow, which mainly consist of aluminum oxide and / or chromium oxide, the axes of which are also predominantly perpendicular to the geometric surface of the semi-finished product. Due to this stem crystal formation, an extraordinarily large surface is created, in which a metallic and / or ceramic coating can be very well anchored.
- profiled, finely crystalline strips of approximately 20 to 200 ⁇ m can be produced in this way, with the aid of cooled copper rolls, possibly up to approximately 500 ⁇ m and more. It is preferable to produce tapes approximately 40 to 70 ⁇ m thick.
- the described stem crystal formation at least in the surface area of the semi-finished product can alternatively be achieved by pouring onto cooled rolls by briefly melting a surface layer of the cast or rolled semi-finished product with subsequent self-cooling.
- a metal strip 50 ⁇ m thick was produced at a cooling rate of 10rate to 105 K / s.
- the material composition is 20% chromium, 5% aluminum, 0.15% cerium, 0.01% lanthanum, the rest iron with small amounts of Si, Mn, C, S, P, Ni as trace elements.
- the tape was then preheated to 900 ° C dry carbon dioxide gas for one minute and then held in air at 925 ° C for 16 hours.
- a cold rolled sheet of the same material composition was also treated after recrystallization annealing.
- the stalk-shaped oxide grains of the cast strip have diameters of approximately 0.2 ⁇ m and lengths of on average approximately 4 ⁇ m and that they are arranged almost uniformly perpendicular to the surface of the metal grains, while the sample produced by rolling is scaly , partially in contact with each other grains of different orientation and length of up to about 3 microns.
- Example 1 A 10 mm thick plate made of the material described in Example 1 was bombarded with an electron beam in such a way that a spot approximately 0.5 mm in diameter was melted down to a depth of 100 ⁇ m. The plate was then treated in CO2 gas at 900 ° C for 1 minute. The procedure was as in Example 1.
- the sample was subjected to several temperature changes, being heated to approximately 1000 ° C. and quenched in an oil bath.
- the stem oxide grains in the area of the melting spot were not attacked by the treatment, the oxide layer on the rest of the sample surface shows individual flaking.
- Example 2 A plate according to Example 2 with a similar melting spot was produced, then an etching was carried out so that the grain boundaries were exposed to a depth of 20 ⁇ m and the procedure according to Example 1 was then continued. It was found that a radiation-like oxide-grain layer of the same quality as in Example 1 had grown on the metal grains which had been partially exposed.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Catalysts (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
- Continuous Casting (AREA)
- Electrical Discharge Machining, Electrochemical Machining, And Combined Machining (AREA)
- Forging (AREA)
- Adornments (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
Abstract
Description
Die Erfindung betrifft ein Verfahren zur Herstellung von metallenem Halbzeug in Form von Draht, Stangen, Knüppeln, Rohren, insbesondere Blechen oder Bändern für Anwendungen, bei denen eine hohe Temperaturwechselbeständigkeit und große Oberfläche und/oder chemische Beständigkeit und/oder geringe Wärmeleitfähigkeit der Oberflächenschicht benötigt wird, insbesondere für Katalysatorträger, Rußfilter, Heizleiter, Aerosolfilter, Auskleidungen von chemischen und Energie umwandelnden Anlagen. Das Halbzeug ist dabei auf der Basis Eisen und/oder Nickel und/oder Cobalt mit 2 bis 16 % Aluminium, 12 bis 30 % Chrom und bis 4 % mindestens eines hochreaktiven Elementes aus der Gruppe Y, Zr, Ti, Ce, Sm, Hf, La, Th, U, V, W, Nb, Mo, Gd, Si, Mg,Ca und/oder deren dispergierte Oxide. Eine Legierung aus diesem Bereich war aus J. Electrochem. Soc., Solid-State Science Technology, Band 131, Nr. 4, Seiten 923 - 931 bekannt. Durch Glühen von Bändern aus dieser Legierung bei Temperaturen über 1000 °C in Sauerstoff können oxidhaltige Oberflächen erzeugt werden.The invention relates to a method for producing semi-finished metal products in the form of wire, rods, billets, tubes, in particular sheet metal or strips, for applications in which a high thermal shock resistance and large surface area and / or chemical resistance and / or low thermal conductivity of the surface layer is required , in particular for catalyst supports, soot filters, heating conductors, aerosol filters, linings of chemical and energy converting systems. The semi-finished product is based on iron and / or nickel and / or cobalt with 2 to 16% aluminum, 12 to 30% chromium and up to 4% of at least one highly reactive element from the group Y, Zr, Ti, Ce, Sm, Hf , La, Th, U, V, W, Nb, Mo, Gd, Si, Mg, Ca and / or their dispersed oxides. An alloy from this area was made from J. Electrochem. Soc., Solid-State Science Technology, Volume 131, No. 4, pages 923-931. By annealing strips of this alloy at temperatures above 1000 ° C in oxygen, oxide-containing surfaces can be created.
Es ist bekannt (Strafford K. N., High temperature Corrosion of alloys Containing rare earth of refractory elements: a review ..., High Temperature Technology Vol. 1 No. 6, Nov. 1983), daß metallene Legierungen des Typs MCrAlX und des Typs MCrAlZX mit M als Eisen und/oder Cobalt und/oder Nickel als Basis und X gewichtsmäßig kleinen Zusätzen hochreaktiver Elemente wie Y, Zr, Ti, Ce, Sm, Hf, La, Th, U, V, W, Ta, Nb, Mo, Gd, Si, Mg, Ca und Z als ein Element oder dessen Oxid aus der Reihe von X, aber ein anderes als das für X jeweils gewählte Element, für eine Verbesserung der oxidischen Schicht-Eigenschaften sorgen. Es wird die Haftung der Oxidschicht verbessert, die aus einzelnen Oxidkörnern besteht, und auch das Oxidations-Verhalten günstig beeinflußt.It is known (Strafford KN, High temperature Corrosion of alloys Containing rare earth of refractory elements: a review ..., High Temperature Technology Vol. 1 No. 6, Nov. 1983) that metal alloys of the MCrAlX and MCrAlZX types with M as iron and / or cobalt and / or nickel as the base and X small additions by weight of highly reactive elements such as Y, Zr, Ti, Ce, Sm, Hf, La, Th, U, V, W, Ta, Nb, Mo, Gd, Si, Mg, Ca and Z as one element or its oxide from the series of X, but a different element than that chosen for X, provide an improvement in the oxide layer properties. The adhesion of the oxide layer, which consists of individual oxide grains, is improved and the oxidation behavior is also favorably influenced.
Es ist ferner bekannt (Ramanarayan T.A., Raghavan, M. und Petkovic-Luton, R., "The Characteristics of Alumina Scales Formed on Fe-Based Yttria-Dispersed Alloys", J. Electrochem. Society, April 1984, Vol. 131 No. 4., 923-931), daß in einer Basislegierung besonders fein dispergierte Oxide der Seltenen Erdmetalle, wie Y₂O₃, einen ähnlich verbessernden Einfluß ausüben.It is also known (Ramanarayan TA, Raghavan, M. and Petkovic-Luton, R., "The Characteristics of Alumina Scales Formed on Fe-Based Yttria-Dispersed Alloys", J. Electrochem. Society, April 1984, Vol. 131 No 4., 923-931) that in a base alloy particularly finely dispersed oxides of rare earth metals, such as Y₂O₃, exert a similarly improving influence.
Die angeführten Legierungen bilden bekanntlich je nach Zusammensetzung entweder überwiegend aus Chromoxid oder aus Aluminiumoxid bestehende Schichten mit hoher Selektivität oder auch aus Al₂O₃-Chromoxid-Mischkristallen bestehende Schichten aus. Bei Verwendungstemperaturen von etwa 900 °C und mehr werden die Legierungen gewählt, die Al₂O₃-Schichten bilden.The alloys mentioned form, depending on the composition, either layers composed predominantly of chromium oxide or aluminum oxide with high selectivity or layers composed of Al₂O₃-chromium oxide mixed crystals. At use temperatures of about 900 ° C and more, the alloys are selected that form Al₂O₃ layers.
Der Nachteil, der nach den beschriebenen Verfahren hergestellten Schichten und Bauteile aus den geschilderten Legierungen, besteht im Fall der Verwendung bei besonders näufigen Temperaturwechseln mit hohen Temperaturdifferenzen darin, daß einzelne Bereiche der Oxidschicht abplatzen. Die so entstehenden Fehlstellen werden von den angegebenen Legierungen bei geeigneten Bedingungen zwar wieder ausgeheilt, das Auftreten von Abplatzungen bei hoher Temperaturwechselbeanspruchung begrenzt aber die Verwendbarkeitsdauer und läßt die heute bekannten Materialien für einige Anwendungen, z.B. als Träger für katalytisch aktive Substanzen, in Sonderheit Edelmetalle für die Entgiftung von Verbrennungsgasen, nicht geeignet erscheinen.The disadvantage of the layers and components made of the described alloys produced by the described methods, in the case of use in the case of particularly frequent temperature changes with high temperature differences, is that individual areas of the oxide layer flake off. The resulting defects are healed again by the specified alloys under suitable conditions, but the occurrence of flaking under high temperature cycling limits the service life and leaves the materials known today for some applications, e.g. do not appear to be suitable as a carrier for catalytically active substances, in particular precious metals for the detoxification of combustion gases.
Ein weiterer Nachteil ist es, daß man Legierungen mit mehr als ca. 6 % Aluminium, z.B. US-A-4 414 023, nicht als Folie durch Walzen herstellen kann bzw. deren Herstellung erhebliche Kosten verursacht. Zur Temperaturbeständigkeit über lange Zeit ist aber eine Ausheilung von Fehlern der Oxidschichten durch aus der Legierung nachzulieferndes Aluminium notwendig und mithin ein möglichst hoher Al-Gehalt sinnvoll.Another disadvantage is that alloys with more than about 6% aluminum, for example US Pat. No. 4,414,023, cannot be produced as a foil by rolling, or their production involves considerable costs. For temperature stability over a long time, however, it is necessary to heal defects in the oxide layers by means of aluminum to be supplied from the alloy, and consequently the highest possible Al content makes sense.
Aus der US-A-4 414 023 ist ein ferritischer rostfreier Stahl bekannt, der warm verarbeitbar und beständig ist gegen Temperaturwechsel, Oxidation und Verzunderung bei erhöhten Temperaturen. Die Eisen-Chrom-Aluminium-Legierung enthält Cer, Lanthan und andere Seltene Erdmetalle und ist geeignet, einen texturierten Aluminiumoxidfilm an der Oberfläche zu bilden. Die Legierung wird in üblicher Weise durch Schmelzen erzeugt. Dabei werden die typischen Stahlverunreinigungen, wie Sauerstoff, Stickstoff und Schwefel vor der Zugabe der Seltenen Erdmetalle zur Schmelze verringert. Jeder herkömmliche Prozeß, einschließlich Lichtbogenöfen, AOD- und Vakuuminduktionsschmelzverfahren ist anwendbar. Die Schmelze wird in Blöcke, Stangen, Bänder oder Bleche gegossen. Der Stahl wird anschließend warm und/oder kaltgewalzt und den üblichen Verfahren unterworfen, wie Entzundern und Glühen. Der ferritische rostfreie Stahl wird dann zur Bildung einer Aluminiumoxid-Oberfläche wärmebehandelt.From US-A-4 414 023 a ferritic stainless steel is known which can be processed hot and is resistant to temperature changes, oxidation and scaling at elevated temperatures. The iron-chromium-aluminum alloy contains cerium, lanthanum and other rare earth metals and is suitable for forming a textured aluminum oxide film on the surface. The alloy is produced in the usual way by melting. The typical steel impurities such as oxygen, nitrogen and sulfur are reduced before the rare earth metals are added to the melt. Any conventional process, including arc furnaces, AOD and vacuum induction melting processes, is applicable. The melt is poured into blocks, bars, strips or sheets. The steel is then hot and / or cold rolled and subjected to the usual procedures such as descaling and annealing. The ferritic stainless steel is then heat treated to form an alumina surface.
Aus der EP 0232793 A1 ist die Ausbildung eines Oxidfilms mit vornehmlich Aluminiumoxidkörnern auf einem aluminiumhaltigen rostfreien Stahl bekannt, indem man die Metallschmelze auf gekühlte Rollen gießt und mit einer Geschwindigkeit von mehr als 1000 K/s erstarren läßt und anschließend das Band oxidierend glüht.From EP 0232793 A1 the formation of an oxide film with primarily aluminum oxide grains on an aluminum-containing stainless steel is known by pouring the molten metal onto cooled rollers and allowing it to solidify at a rate of more than 1000 K / s and then oxidizing the strip.
Aufgabe der Erfindung ist es, ein metallenes Halbzeug zu schaffen, das vorzugsweise ohne Zwischenschicht (wash coat) einen temperaturwechselbeständigen Haftgrund für einen katalytisch wirkenden Überzug darstellt. Die Aufgabe umfaßt ferner die Schaffung eines Verfahrens, welches in möglichst einfacher Weise zu einem metallischen Halbzeug mit der erwähnten Eigenschaft führt.The object of the invention is to provide a semi-finished metal product which, preferably without an intermediate layer (wash coat), represents a temperature change-resistant adhesive base for a catalytically active coating. The task also includes the creation of a method which leads in the simplest possible way to a metallic semi-finished product with the property mentioned.
Zur Lösung der gestellten Aufgabe wird für ein metallenes Halbzeug auf der Basis Eisen und/oder Nickel und/oder Cobalt mit 2 bis 16 % Aluminium, 12 bis 30 % Chrom und bis 4 % mindestens eines hochreaktiven Elementes aus der Gruppe Y, Zr, Ti, Ce, Sm, Hf, La, Th, U, V, W, Ta, Nb, Mo, Gd, Si, Mg, Ca und/oder deren dispergierte Oxide, vorzugsweise mindestens 0,01 % dieser Elemente bzw. Oxide, sowie unvermeidbare Verunreinigungen erfindungsgemäß vorgeschlagen, daß das Halbzeug aus dem schmelzflüssigen Zustand in einer zur geometrischen Oberfläche überwiegend parallelen Front mit einer Abkühlungsgeschwindigkeit von 10³ bis 10⁶ K/s erstarrt wird, dann zunächst bei einer Temperatur von 800 bis 1000 °C kurzzeitig in einem Sauerstoff in gebundener Form enthaltenen Gas, insbesondere CO₂, unter sich dabei einstellenden reduzierenden Bedingungen und anschliessend im Temperaturbereich von 800 bis 1000 °C bis zu 25 h an Luft geglüht wird, wobei mindestens im Oberflächenbereich des Halbzeugs metallene Stengelkristalle gebildet sind, aus denen heraus überwiegend aus Aluminumoxid und/oder Chromoxid bestehende Stengelkristalle gewachsen sind, wobei die Achsen beider Stengelkristalltypen übewiegend senkrecht zur geometrischen Oberfläche des Halbzeugs stehen.To achieve the object, a semi-finished metal product based on iron and / or nickel and / or cobalt with 2 to 16% aluminum, 12 to 30% chromium and up to 4% of at least one highly reactive element from the group Y, Zr, Ti , Ce, Sm, Hf, La, Th, U, V, W, Ta, Nb, Mo, Gd, Si, Mg, Ca and / or their dispersed oxides, preferably at least 0.01% of these elements or oxides, and Inevitable impurities proposed according to the invention that the semifinished product is solidified from the molten state in a front, which is predominantly parallel to the geometric surface, with a cooling rate of 10³ to 10⁶ K / s, then briefly in a bonded oxygen at a temperature of 800 to 1000 ° C Form contained gas, in particular CO₂, is set under reducing conditions and then in the temperature range from 800 to 1000 ° C for up to 25 h in air, at least in the surface area of Semi-finished metal stem crystals are formed, from which stem crystals consisting predominantly of aluminum oxide and / or chromium oxide have grown, the axes of both types of stem crystal being predominantly perpendicular to the geometric surface of the semi-finished product.
Normale Stahlverunreinigungen sind Kohlenstoff, Stickstoff, Sauerstoff, Phosphor, Schwefel, Mangan, Kupfer und Nickel.Normal steel contaminants are carbon, nitrogen, oxygen, phosphorus, sulfur, manganese, copper and nickel.
Aus den beigefügten Schliffbildern ist die Oberflächenstruktur deutlich erkennbar.The surface structure can be clearly seen from the attached micrographs.
Bild 1 zeigt eine nach herkömmlichen Verfahren erzeugte Halbzeug-Oberfläche mit unregelmäßig liegenden whiskerähnlichen oxidischen Stengelkristallen.Figure 1 shows a semi-finished product surface produced using conventional methods with irregularly lying whisker-like oxidic stem crystals.
Bild 2 zeigt die Halbzeug-Oberfläche, wie sie bei Ausübung des erfindungsgemäßen Verfahrens gebildet ist. Die großen Bereiche sind die metallenen Stengelkristalle, aus deren Oberfläche haarähnlich die oxidischen Stengelkristalle gewachsen sind.Figure 2 shows the semi-finished product surface as it is formed when the method according to the invention is carried out. The large areas are the metal stem crystals, from the surface of which the oxidic stem crystals have grown like hair.
Bild 3 zeigt die oxidischen Stengelkristalle in gegenüber Bild 2 10-facher Vergrößerung. Danach liegen die Achsen der oxidischen Stengelkristalle überwiegend senkrecht zur geometrischen Oberfläche des Halbzeugs, die durch die Oberflächen der metallenen Stengelkristalle gebildet wird.Figure 3 shows the oxide stem crystals in 10 times magnification compared to Figure 2. According to this, the axes of the oxide stem crystals are predominantly perpendicular to the geometric surface of the semi-finished product, which is formed by the surfaces of the metal stem crystals.
Gehalte von 14 bis 25 % Chrom und 5 bis 9 % Aluminium in der Matrix aus Eisen und/oder Nickel und/oder Cobalt haben sich als besonders geeignet zur Ausbildung der überwiegend aus Aluminium- und Chromoxid oder in Abhängigkeit von den Glühbedingungen praktisch ausschließlich aus Aluminiumoxid bestehenden oxidischen Stengelkristalle erwiesen. Weitere Elemente, die die Stengelkristallbildung nicht beeinträchtigen oder sie sogar begünstigen, können außer den genannten Elementen enthalten sein.Contents of 14 to 25% chromium and 5 to 9% aluminum in the matrix made of iron and / or nickel and / or cobalt have proven to be particularly suitable for the formation mainly of aluminum and chromium oxide or, depending on the annealing conditions, practically exclusively of aluminum oxide existing oxidic stem crystals. In addition to the elements mentioned, other elements which do not impair or even favor the formation of stem crystals can be present.
Der mittlere Korndurchmesser D der metallenen Stengelkristalle kann 5 bis 50 µm betragen. Vorzugsweise wählt man je nach Legierung und Wandstärke die Abkühlrate so, daß der mittlere Korndurchmesser D = 5 bis 30 µm beträgt. Die Länge der Körner sollte sein L = 15 µm bis zur Dicke des Bandes, vorzugsweise L = 20 bis 100 µm, mit L : D ≧ 3.The average grain diameter D of the metal stem crystals can be 5 to 50 µm. Depending on the alloy and wall thickness, the cooling rate is preferably chosen so that the average grain diameter is D = 5 to 30 μm. The length of the grains should be L = 15 µm to the thickness of the tape, preferably L = 20 to 100 µm, with L: D ≧ 3.
Es hat sich gezeigt, daß sich, durch die kristallographisch überwiegend einheitliche Ausrichtung der Körner des Gefüges bedingt, eng aneinander stehende aber separate Oxidkörner mit einem Durchmesser je nach Züchtungsbedingungen von d = 0,05 bis 3 µm, und Längen von l = 0,5 bis 15 µm mit l : d ≧ 3 bilden.It has been shown that, due to the crystallographically predominantly uniform alignment of the grains of the structure, there are closely spaced but separate oxide grains with a diameter of d = 0.05 to 3 μm, depending on the growing conditions, and lengths of l = 0.5 form up to 15 µm with l: d ≧ 3.
Durch die Erfindung wird ein metallenes Halbzeug geschaffen, bei dem mindestens im Oberflächenbereich durch die gerichtete Erstarrung der Metallegierung metallene Stengelkristallite gebildet werden. Durch die hohe Abkühlungsgeschwindigkeit und thermische Behandlung bedingt, fungieren die Zusatzelemente aus der vorgenannten Gruppe X, die hochreaktiv sind, d.h. hochsauerstoffaffin sind, bzw. deren Oxide, die in fein verteilter Form im Oberflächenbereich vorliegen, bei der anschließenden Wärmebehandlung als Keime. Gleichzeitig sorgen sie als eine Art Dübel für eine hohe Haftfestigkeit der im Anschluß thermisch gezüchteten oxidischen Stengelkristallite. Eine weiter verbesserte Keimbildung wird dadurch erzielt, daß man als erste thermische Behandlungsstufe kurzzeitig unter reduzierenden oder sich bei dieser Behandlung einstellenden reduzierenden Bedingungen erhitzt. Anschließend erfolgt die langzeitige Glühbehandlung unter oxidierenden Bedingungen, vorzugsweise an Luft, bei der die oxidischen Stengelkristallite wachsen, die überwiegend aus Aluminiumoxid und/oder Chromoxid bestehen, deren Achsen ebenfalls überwiegend senkrecht zur geometrischen Oberfläche des Halbzeugs stehen. Aufgrund dieser Stengelkristallbildung wird eine außerordentlich große Oberfläche geschaffen, in der sich ein metallener und/oder keramischer Überzug sehr gut verankern läßt.The invention provides a semi-finished metal product in which metal stem crystallites are formed at least in the surface area by the directional solidification of the metal alloy. Due to the high cooling rate and thermal treatment, the additional elements from the aforementioned group X, which are highly reactive, i.e. are highly oxygen-affine, or their oxides, which are present in finely divided form in the surface area, in the subsequent heat treatment as germs. At the same time, as a kind of dowel, they ensure a high level of adhesive strength for the thermally grown oxidic stem crystallites. A further improved nucleation is achieved by briefly heating as the first thermal treatment stage under reducing conditions or those that occur during this treatment. This is followed by the long-term annealing treatment under oxidizing conditions, preferably in air, in which the oxidic stem crystallites grow, which mainly consist of aluminum oxide and / or chromium oxide, the axes of which are also predominantly perpendicular to the geometric surface of the semi-finished product. Due to this stem crystal formation, an extraordinarily large surface is created, in which a metallic and / or ceramic coating can be very well anchored.
Die Größe der Körner des Metallgefüges wird durch die Abkünlgeschwindigkeit und den Wärmeinhalt der Metallschmelze bestimmt. Zur Herstellung von Bändern mit ca. 50 µm Dicke, wie sie z.B. als Träger für Abgaskatalysatoren für Kraftfahrzeuge und Kraftwerke benötigt werden, hat es sich als günstig herausgestellt, mit einer Vorrichtung zu arbeiten, bei der unter einem Tiegel, der einen langen, dünnen Spalt als Düse aufweist, wobei der Spalt ggf. mit Hilfe einer angeschrägten keramischen Stopfenstange geöffnet werden kann, eine oder zwei Rollen angeordnet sind. Die Rolle oder die Rollen können an ihrer Umfangsfläche eine vorgegebene Welligkeit aufweisen, so daß der Metallstrahl auf der einen Rolle bzw. im vorgegebenen Spalt zwischen den beiden Rollen schon in der für den Einsatzzweck notwendigen geometrischen Gestalt erstarrt. Die Anordnung hat folgende Vorteile:
- das Metallband braucht im wesentlichen nicht mehr plastisch verformt zu werden; Bereiche plastischer Verformung führen bekanntlich zu unkontrolliertem Wachstum der Körner des Metallgefüges bei den anschließenden Behandlungsschritten bei erhöhten Temperaturen und damit zur unregelmäßigen Ausbildung der Körner der Oxidschicht;
- die Rolle bzw. Rollen können aus einem Material wie Stahl oder Keramik mit einer geringeren Wärmeleitfähigkeit hergestellt werden, als dies mit Kupferrollen für die Herstellung amorpher Bänder notwendig ist;
- die Rolle bzw. Rollen werden wenn nötig mit Hilfe von erwärmtem, umlaufendem Öl auf eine vorgegebene Temperatur gehalten, wodurch auf diese Weise die gewünschte Kristallgröße des Metallgefüges eingestellt wird und eine besondere Wärmenachbehandlung zur Korngrößeneinstellung entfallen kann.
- the metal strip essentially no longer needs to be plastically deformed; Areas of plastic deformation are known to lead to uncontrolled growth of the grains of the metal structure in the subsequent treatment steps at elevated temperatures and thus to the irregular formation of the grains of the oxide layer;
- the roll or rolls can be made of a material such as steel or ceramic with a lower thermal conductivity than is necessary with copper rolls for the production of amorphous strips;
- if necessary, the roller or rollers are kept at a predetermined temperature with the aid of heated, circulating oil, as a result of which the desired crystal size of the metal structure is set and a special heat treatment for grain size adjustment can be omitted.
Es hat sich nun herausgestellt, daß man auf diese Weise profilierte, feinkristalline Bänder von ca. 20 bis 200 µm, mit Hilfe von gekühlten Kupferrollen auch möglicherweise bis zu etwa 500 µm und mehr herstellen kann. Vorzugsweise stellt man Bänder von ca. 40 bis 70 µm Dicke her.It has now been found that profiled, finely crystalline strips of approximately 20 to 200 μm can be produced in this way, with the aid of cooled copper rolls, possibly up to approximately 500 μm and more. It is preferable to produce tapes approximately 40 to 70 µm thick.
So ist es auf diese Weise möglich, Aluminiumoxid-Schichten zu erzeugen, die aus einzelnen voneinander getrennt aber weitgehend gleichförmig gewachsenen Oxid-Körnern mit einem Durchmesser von vorzugsweise d = 0,1 µm bis 0,3 µm und einer Länge l = 4 bis 15 µm bestehen, so daß hierauf die Abscheidung von katalytisch aktiven Substanzen vorgenommen werden kann, ohne daß eine zusätzliche Zwischenschicht (wash coat), wie z.B. bei rein oxidischen Katalysator-Trägern, notwendig ist.In this way it is possible to produce aluminum oxide layers which consist of individual oxide grains which have grown separately but largely uniformly and have a diameter of preferably d = 0.1 μm to 0.3 μm and a length l = 4 to 15 µm exist, so that the deposition of catalytically active substances can be carried out without an additional intermediate layer (wash coat), such as in the case of purely oxidic catalyst supports.
Die geschilderte Stengelkristallbildung mindestens im Oberflächenbereich des Halbzeugs kann alternativ zu dem vorstehend erwähnten Gießen auf gekühlte Walzen auch durch kurzzeitiges Aufschmelzen einer Oberflächenschicht des gegossenen order gewalzten Halbzeugs mit anschließendem Selbstabkühlen erreicht werden.The described stem crystal formation at least in the surface area of the semi-finished product can alternatively be achieved by pouring onto cooled rolls by briefly melting a surface layer of the cast or rolled semi-finished product with subsequent self-cooling.
Die Erfindung wird im folgenden anhand von drei Ausführungsbeispielen erläutert.The invention is explained below using three exemplary embodiments.
Es wurde mit Hilfe einer Rolle aus Stahl, die durch einen Ölkreislauf auf einer konstanten Temperatur gehalten wurde, ein Metallband von 50 µm Dicke bei einer Abkühlrate von 10⁵ bis 10⁴ K/s hergestellt. Die Materialzusammensetzung ist 20 % Chrom, 5 % Aluminium, 0,15 % Cer, 0,01 % Lanthan, Rest Eisen mit geringen Anteilen an Si, Mn, C, S, P, Ni als Spurenelemente.With the help of a roller made of steel, which was kept at a constant temperature by an oil circuit, a metal strip 50 µm thick was produced at a cooling rate of 10rate to 10⁵ K / s. The material composition is 20% chromium, 5% aluminum, 0.15% cerium, 0.01% lanthanum, the rest iron with small amounts of Si, Mn, C, S, P, Ni as trace elements.
Das Band wurde anschließend einer Wärmevorbehandlung von 900 °C eine Minute lang trockenem Kohlendioxidgas ausgesetzt und anschließend an Luft bei 925 °C sechzehn Stunden gehalten. Eine kalt gewalzte Folie gleicher Materialzusammensetzung wurde nach einer Rekristallisationsglühung ebenso behandelt.The tape was then preheated to 900 ° C dry carbon dioxide gas for one minute and then held in air at 925 ° C for 16 hours. A cold rolled sheet of the same material composition was also treated after recrystallization annealing.
Es zeigt sich, daß die stengelförmigen Oxid-Körner des gegossenen Bandes Durchmesser von ca. 0,2 µm und Längen von im Mittel ca. 4 µm aufweisen und sie nahezu einheitlich senkrecht zur Oberfläche der Metallkörner angeordnet sind, während die durch Walzen hergestellte Probe schuppenförmige, untereinander zum Teil in Kontakt stehende Körner unterschiedlicher Ausrichtung und Länge von bis zu ca. 3 µm aufweist.It can be seen that the stalk-shaped oxide grains of the cast strip have diameters of approximately 0.2 μm and lengths of on average approximately 4 μm and that they are arranged almost uniformly perpendicular to the surface of the metal grains, while the sample produced by rolling is scaly , partially in contact with each other grains of different orientation and length of up to about 3 microns.
Es wurde eine 10 mm dicke Platte aus dem im Beispiel 1 beschriebenen Material mit einem Elektronenstrahl so beschossen, daß ein Fleck von ca. 0,5 mm Durchmesser bis zu 100 µm tief aufgeschmolzen wurde. Die Platte wurde anschließend 1 Minute in CO₂-Gas bei 900 °C behandelt. Im weiteren wurde wie im Beispiel 1 verfahren.A 10 mm thick plate made of the material described in Example 1 was bombarded with an electron beam in such a way that a spot approximately 0.5 mm in diameter was melted down to a depth of 100 μm. The plate was then treated in CO₂ gas at 900 ° C for 1 minute. The procedure was as in Example 1.
Es zeigte sich, daß die erzeugten Oxid-Körner bzw. Whisker im Bereich des Schmelzfleckes eine ähnlich gute Qualität wie die der gegossenen Probe nach dem Beispiel 1 aufweisen.It was found that the oxide grains or whiskers produced in the area of the melting spot have a similar quality to that of the cast sample according to Example 1.
Die Probe wurde mehreren Temperaturwechseln ausgesetzt, wobei sie auf ca. 1000 °C erhitzt in einem Ölbad abgeschreckt wurde. Die Stengel-Oxid-Körner des Bereiches des Schmelzfleckes wurden durch die Behandlung nicht angegriffen, die Oxidschicht der übrigen Probenoberfläche zeigt einzelne Abplatzungen.The sample was subjected to several temperature changes, being heated to approximately 1000 ° C. and quenched in an oil bath. The stem oxide grains in the area of the melting spot were not attacked by the treatment, the oxide layer on the rest of the sample surface shows individual flaking.
Es wurde eine Platte nach Beispiel 2 mit einem ähnlichen Schmelzfleck hergestellt, anschließend eine Ätzung vorgenommen, so daß die Korngrenzen bis in eine Tiefe von 20 µm freigelegt wurden und anschließend wurde weiter nach Beispiel 1 verfahren. Es zeigte sich, daß auf den so teilweise freigelegten Metallkörnern eine strahlenförmige Oxid-Korn-Schicht gleicher Qualität des Beispiels 1 gewachsen ist.A plate according to Example 2 with a similar melting spot was produced, then an etching was carried out so that the grain boundaries were exposed to a depth of 20 μm and the procedure according to Example 1 was then continued. It was found that a radiation-like oxide-grain layer of the same quality as in Example 1 had grown on the metal grains which had been partially exposed.
Auf diese Weise gelingt es, eine besonders große Oberfläche zu erzeugen, so daß zur Verwendung als Katalysatorträger vorzugsweise keine bzw. nur ein sehr dünne (20 um dicke) Zwischenschicht (wash coat) mehr nötig erscheint.In this way, it is possible to produce a particularly large surface area, so that preferably no or only a very thin (20 μm thick) intermediate layer (wash coat) appears to be necessary for use as a catalyst support.
Es ist möglich, die so erzeugte Oxidschicht durch Besanden, Schlickern, Flamm- oder Plasmaspritzen oder auch durch andere bekannte Methoden noch zusätzlich mit Keramik oder Metallen zu beschichten. Durch die Abfolge der Schritte Schlickern-Trocknen-Plasmaspritzen lassen sich sogar nahezu gasdichte Oxidschichten aufbringen, die nur über die stengelförmigen Oxidkörner fest mit dem Metallkörper verbunden sind und deshalb eine hohe Temperaturwechselbeständigkeit aufweisen.It is possible to additionally coat the oxide layer produced in this way with sanding, slip, flame or plasma spraying or also by other known methods with ceramic or metals. The sequence of the steps of slip-drying-plasma spraying even allows almost gas-tight oxide layers to be applied, which are only firmly connected to the metal body via the stem-shaped oxide grains and therefore have a high resistance to temperature changes.
Claims (9)
characterized in that the semi-finished product is allowed to solidify from the molten condition predominantly parallel with the geometrical surface at a cooling speed of 10³ to 10⁶ K/sec, whereafter annealing is performed first briefly at a temperature of 800 to 1000°C in a gas, more particularly CO₂, containing oxygen in the bonded form, in reducing conditions produced thereby, and annealing then being performed in air over the same temperature range for up to 25 hours, metal fringe crystals being formed at least in the surface zone of the semi-finished product, from which fringe crystals consisting mainly of aluminium oxide and/or chromium oxide are grown, the axes of the two kinds of fringe crystal lying predominantly perpendicularly to the geometrical surface of the semi-finished product.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT87102472T ATE65552T1 (en) | 1986-03-01 | 1987-02-21 | METAL SEMI-FINISHED PRODUCT, METHOD OF MANUFACTURE AND USE OF THE SEMI-FINISHED PRODUCT. |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE19863606804 DE3606804A1 (en) | 1986-03-01 | 1986-03-01 | METALLIC SEMI-FINISHED PRODUCT AND METHOD FOR THE PRODUCTION AND USE THEREOF |
DE3606804 | 1986-03-01 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0236823A2 EP0236823A2 (en) | 1987-09-16 |
EP0236823A3 EP0236823A3 (en) | 1988-05-25 |
EP0236823B1 true EP0236823B1 (en) | 1991-07-24 |
Family
ID=6295321
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP87102472A Expired - Lifetime EP0236823B1 (en) | 1986-03-01 | 1987-02-21 | Metallic semi-finished product, process for its manufacture and uses of the semi-finished product |
Country Status (6)
Country | Link |
---|---|
US (1) | US4798631A (en) |
EP (1) | EP0236823B1 (en) |
JP (1) | JPH0660386B2 (en) |
KR (1) | KR940003503B1 (en) |
AT (1) | ATE65552T1 (en) |
DE (2) | DE3606804A1 (en) |
Families Citing this family (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6411957A (en) * | 1987-07-04 | 1989-01-17 | Kawasaki Steel Co | Manufacture of stainless steel having high-temperature oxidation film excellent in corrosion resistance |
US4915751A (en) * | 1988-09-06 | 1990-04-10 | General Motors Corporation | Accelerated whisker growth on iron-chromium-aluminum alloy foil |
JP3386848B2 (en) * | 1992-06-10 | 2003-03-17 | 株式会社島津製作所 | Exhaust gas purification device and method of manufacturing the same |
US5476554A (en) * | 1993-05-20 | 1995-12-19 | Kawasaki Steel Corporation | FE-CR-AL alloy foil having high oxidation resistance for a substrate of a catalytic converter and method of manufacturing same |
JP3374173B2 (en) * | 1999-10-21 | 2003-02-04 | 独立行政法人物質・材料研究機構 | Method for producing heat-resistant intermetallic compound Ni3Al foil having ductility at room temperature and heat-resistant intermetallic compound Ni3Al foil having ductility at room temperature |
JP3611107B2 (en) * | 2000-04-12 | 2005-01-19 | セイコーエプソン株式会社 | Cooling roll |
JP3728396B2 (en) | 2000-04-12 | 2005-12-21 | セイコーエプソン株式会社 | Manufacturing method of magnet material |
JP3587140B2 (en) | 2000-07-31 | 2004-11-10 | セイコーエプソン株式会社 | Method for producing magnet powder, magnet powder and bonded magnet |
JP4554794B2 (en) * | 2000-08-23 | 2010-09-29 | 日本冶金工業株式会社 | Stainless steel with insulating layer |
EP1344907A1 (en) * | 2002-03-12 | 2003-09-17 | Capital Technology GmbH | Device for removing carbon particles from exhaust gases |
EP1935996A1 (en) * | 2002-11-04 | 2008-06-25 | Paralloy Limited | High temperature resistant alloys |
GB2394959A (en) * | 2002-11-04 | 2004-05-12 | Doncasters Ltd | Hafnium particle dispersion hardened nickel-chromium-iron alloys |
JP4614063B2 (en) * | 2004-05-20 | 2011-01-19 | 日産自動車株式会社 | Whisker forming body and method for producing whisker forming body |
JP4788878B2 (en) * | 2004-07-01 | 2011-10-05 | 日産自動車株式会社 | Whisker coating material and manufacturing method thereof |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0232793A1 (en) * | 1986-01-30 | 1987-08-19 | Nippon Steel Corporation | Stainless steel ribbon for use as a catalyst carrier for automobile exhaust gas and method for producing same |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US3027252A (en) * | 1959-09-29 | 1962-03-27 | Gen Electric | Oxidation resistant iron-chromium alloy |
US3298826A (en) * | 1964-04-06 | 1967-01-17 | Carl S Wukusick | Embrittlement-resistant iron-chromium-aluminum-yttrium alloys |
JPS4945456B1 (en) * | 1969-06-25 | 1974-12-04 | ||
US4331631A (en) * | 1979-11-28 | 1982-05-25 | General Motors Corporation | Enhanced oxide whisker growth on peeled Al-containing stainless steel foil |
US4414023A (en) * | 1982-04-12 | 1983-11-08 | Allegheny Ludlum Steel Corporation | Iron-chromium-aluminum alloy and article and method therefor |
GB2158746A (en) * | 1984-05-14 | 1985-11-20 | Olin Corp | Apparatus and process for rolling spin cast strip |
-
1986
- 1986-03-01 DE DE19863606804 patent/DE3606804A1/en active Granted
-
1987
- 1987-02-21 EP EP87102472A patent/EP0236823B1/en not_active Expired - Lifetime
- 1987-02-21 DE DE8787102472T patent/DE3771526D1/en not_active Expired - Fee Related
- 1987-02-21 AT AT87102472T patent/ATE65552T1/en not_active IP Right Cessation
- 1987-02-25 US US07/018,545 patent/US4798631A/en not_active Expired - Fee Related
- 1987-02-28 KR KR1019870001778A patent/KR940003503B1/en not_active IP Right Cessation
- 1987-02-28 JP JP62044144A patent/JPH0660386B2/en not_active Expired - Lifetime
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0232793A1 (en) * | 1986-01-30 | 1987-08-19 | Nippon Steel Corporation | Stainless steel ribbon for use as a catalyst carrier for automobile exhaust gas and method for producing same |
Non-Patent Citations (1)
Title |
---|
K.N. STRAFFORD, "High Temperature Technology, vol. 1, No. 6, Nov. 1983, p. 307-318 * |
Also Published As
Publication number | Publication date |
---|---|
KR870009050A (en) | 1987-10-23 |
ATE65552T1 (en) | 1991-08-15 |
DE3771526D1 (en) | 1991-08-29 |
DE3606804A1 (en) | 1987-09-10 |
JPS62290857A (en) | 1987-12-17 |
EP0236823A2 (en) | 1987-09-16 |
DE3606804C2 (en) | 1989-03-30 |
US4798631A (en) | 1989-01-17 |
JPH0660386B2 (en) | 1994-08-10 |
EP0236823A3 (en) | 1988-05-25 |
KR940003503B1 (en) | 1994-04-23 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
DE10005861C2 (en) | Nickel-based metallic material and process for its production | |
EP0236823B1 (en) | Metallic semi-finished product, process for its manufacture and uses of the semi-finished product | |
DE3011152C2 (en) | ||
DE3242607C2 (en) | ||
EP3004408B1 (en) | Method for producing a metal film | |
EP3004409B1 (en) | Method for producing a metal film | |
DE2606581A1 (en) | PROCESS FOR MANUFACTURING METAL ALLOY FEMS | |
EP2137330A2 (en) | Metal foil | |
DE3813685A1 (en) | ROLLED, STAINLESS STEEL FILM WITH A HIGH ALUMINUM CONTENT FOR USE AS A SUBSTRATE OF A CATALYST CARRIER | |
EP2127472B1 (en) | Use of an iron-chromium-aluminium alloy with long service life and minor changes in heat resistance | |
DE19928842C2 (en) | Ferritic alloy | |
DE3330814C2 (en) | Process for the manufacture of aluminum products | |
DE10002933C1 (en) | Iron-chromium-aluminum foil production, used e.g. as support material for exhaust gas treatment catalysts, comprises coating one or both sides of supporting strip with aluminum or aluminum alloys, and carrying out homogenizing treatment | |
DE10143680C1 (en) | Process for the production of metal strips with high-grade cube texture | |
EP0302252A2 (en) | Filter for small particles | |
DE2747660C2 (en) | A method of manufacturing non-oriented silicon steel sheets with high magnetic induction and low core loss | |
EP1922426B1 (en) | Method for producing and using a nickel-based semi-finished product having a recrystallisation cube structure | |
EP0659901B1 (en) | Cobalt based alloy target for magnetron sputtering apparatus | |
DE2928059C2 (en) | ||
EP0327831A2 (en) | Method and device for increasing the thermal fatigue resistance of heat-conducting materials | |
DE4035114C2 (en) | Fe-Cr-Ni-Al ferrite alloys | |
DE3911619A1 (en) | Ductile semi-finished iron-chrome aluminum base and its use as a carrier material for catalysts | |
DE102004060900A1 (en) | Nickel-based semi-finished product with cube texture and process for its production | |
DE4222026C1 (en) | Semi-finished prod. mfr. used as catalyst supports - by coating starting material, e.g. ferritic stainless steel, with at least one chromium@ layer and diffusion heat treating | |
DE2656161C2 (en) | Process for the production of grain-oriented electrical steel sheet |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Kind code of ref document: A2 Designated state(s): AT BE CH DE ES FR GB IT LI NL SE |
|
PUAL | Search report despatched |
Free format text: ORIGINAL CODE: 0009013 |
|
AK | Designated contracting states |
Kind code of ref document: A3 Designated state(s): AT BE CH DE ES FR GB IT LI NL SE |
|
17P | Request for examination filed |
Effective date: 19881011 |
|
17Q | First examination report despatched |
Effective date: 19900115 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE CH DE ES FR GB IT LI NL SE |
|
REF | Corresponds to: |
Ref document number: 65552 Country of ref document: AT Date of ref document: 19910815 Kind code of ref document: T |
|
ET | Fr: translation filed | ||
GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) | ||
REF | Corresponds to: |
Ref document number: 3771526 Country of ref document: DE Date of ref document: 19910829 |
|
ITF | It: translation for a ep patent filed |
Owner name: SOCIETA' ITALIANA BREVETTI S.P.A. |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 19911104 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed | ||
EAL | Se: european patent in force in sweden |
Ref document number: 87102472.5 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 19950201 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 19950203 Year of fee payment: 9 Ref country code: CH Payment date: 19950203 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 19950208 Year of fee payment: 9 Ref country code: AT Payment date: 19950208 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 19950228 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 19950306 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 19950322 Year of fee payment: 9 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Effective date: 19960221 Ref country code: AT Effective date: 19960221 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SE Effective date: 19960222 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 19960228 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 19960228 Ref country code: BE Effective date: 19960228 |
|
BERE | Be: lapsed |
Owner name: THYSSEN A.G. VORM. AUGUST THYSSEN-HUTTE Effective date: 19960228 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Effective date: 19960901 |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 19960221 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FR Effective date: 19961031 |
|
NLV4 | Nl: lapsed or anulled due to non-payment of the annual fee |
Effective date: 19960901 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DE Effective date: 19961101 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: ST |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED. Effective date: 20050221 |