EP2893049B1 - Blech aus ferritischem edelstahl, verfahren zur herstellung und verwendung, insbesondere in abgasleitungen - Google Patents

Blech aus ferritischem edelstahl, verfahren zur herstellung und verwendung, insbesondere in abgasleitungen Download PDF

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EP2893049B1
EP2893049B1 EP12766456.3A EP12766456A EP2893049B1 EP 2893049 B1 EP2893049 B1 EP 2893049B1 EP 12766456 A EP12766456 A EP 12766456A EP 2893049 B1 EP2893049 B1 EP 2893049B1
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comprised
rolled
temperature
hot
trace amounts
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EP2893049A1 (de
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Pierre-Olivier Santacreu
Claudine MIRAVAL
Saghi SAEDLOU
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Aperam Stainless France SA
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Aperam Stainless France SA
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    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D7/00—Casting ingots, e.g. from ferrous metals
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    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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    • 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
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    • C—CHEMISTRY; METALLURGY
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    • C—CHEMISTRY; METALLURGY
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    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N3/00—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust
    • F01N3/08—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous
    • F01N3/10—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous by thermal or catalytic conversion of noxious components of exhaust
    • F01N3/18—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous by thermal or catalytic conversion of noxious components of exhaust characterised by methods of operation; Control
    • F01N3/20—Exhaust or silencing apparatus having means for purifying, rendering innocuous, or otherwise treating exhaust for rendering innocuous by thermal or catalytic conversion of noxious components of exhaust characterised by methods of operation; Control specially adapted for catalytic conversion ; Methods of operation or control of catalytic converters
    • F01N3/2066—Selective catalytic reduction [SCR]
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2610/00—Adding substances to exhaust gases
    • F01N2610/02—Adding substances to exhaust gases the substance being ammonia or urea

Definitions

  • the invention relates to a ferritic stainless steel, its manufacturing process, and its use for the manufacture of mechanically welded parts subjected to high temperatures, such as elements of exhaust lines of internal combustion engines.
  • these parts are subjected to temperatures between 150 and 700 ° C, and to a projection of a mixture of urea and water (typically 32.5% urea - 67.5% water ), or a mixture of ammonia and water, or pure ammonia.
  • a mixture of urea and water typically 32.5% urea - 67.5% water
  • ammonia and water typically pure ammonia.
  • the decomposition products of urea and ammonia can also degrade parts of the exhaust system.
  • the mechanical resistance at high temperature must also be adapted to the thermal cycles associated with the phases of acceleration and deceleration of the engines.
  • the metal must have good cold formability to be shaped by bending or hydroforming, as well as good weldability.
  • Ferritic 17% Cr stainless steels are thus known, stabilized with 0.14% titanium and 0.5% niobium (type EN 1.4509, AISI 441) allowing use up to 950 ° C.
  • Ferritic stainless steels with a lower chromium content are also known, for example steels with 12% Cr stabilized with 0.2% titanium (type EN 1.4512 AISI 409) for maximum temperatures below 850 ° C, steels at 14% Cr stabilized with 0.5% niobium without titanium (type EN 1.4595) for maximum temperatures below 900 ° C. These have a high temperature resistance equivalent to that of the previous shades, but better formability.
  • ferritic grades cited corrode excessively at the grain boundaries, in the presence of a projection of a mixture of water, d 'urea and ammonia and for temperatures between 150 and 700 ° C. This makes these steels insufficiently suitable for their use in exhaust lines equipped with urea or ammonia depollution systems, as is often the case, for example, on diesel-powered vehicles.
  • the document JP-A-2011-105976 describes a stainless steel pipe for a wastewater discharge pipe, the weld area of which (carried out by the TIG process) has excellent resistance to corrosion by chlorides and H2S. To this end, the scale formed during welding is not removed.
  • the object of the present invention is to resolve the corrosion problems mentioned above. It aims in particular to make available to users of engines equipped with a urea or ammonia exhaust gas depollution system a ferritic stainless steel which has, compared to the grades known for this purpose, improved resistance to corrosion by a mixture of water, urea and ammonia.
  • This steel must also maintain good resistance to heat, that is to say a high resistance to creep, thermal fatigue and oxidation at operating temperatures that vary periodically and can reach several hundred ° C, as well as a suitability for cold forming and welding equivalent to that of grade EN 1.4509 AISI 441, i.e. guaranteeing a minimum elongation at break of 28% in tension, for mechanical properties in tension typically 300 MPa for the elastic limit Re and 490 MPa for the tensile strength Rm.
  • the subject of the invention is also two methods of manufacturing a ferritic stainless steel sheet of the above type.
  • the hot rolling temperature is between 1180 and 1200 ° C.
  • the temperature of the final annealing is between 1050 and 1090 ° C.
  • a subject of the invention is also the use of such a steel sheet for the manufacture of parts involving shaping and welding and intended to be subjected to a periodic use temperature of between 150 ° C and 700. ° C and a projection of a mixture of water, urea and ammonia or a projection of urea or ammonia.
  • They may in particular be parts of the exhaust lines of internal combustion engines equipped with a catalytic system for reducing nitrogen oxides by injection of urea or ammonia.
  • the invention is based on the use of ferritic stainless steel sheets having the composition and the structure specified, which the inventors have discovered to be particularly well suited to solving the technical problems mentioned above. .
  • the average grain size of between 25 and 65 ⁇ m is an important feature of the invention, and it is controlled both by the presence of nitrides and carbonitrides of titanium and niobium and by the temperature of the final annealing. .
  • the carbon would be likely to increase the mechanical characteristics at high temperature, in particular the creep resistance.
  • carbon tends to precipitate in the form of M 23 C 6 or M 7 C 3 carbides between 600 ° C and 900 ° C approximately, for example chromium carbides.
  • This precipitation generally located at the grain boundaries, can lead to a depletion of chromium in the vicinity of these joints, and therefore to sensitization of the metal to intergranular corrosion.
  • This sensitization can be found in particular in Heat Affected Areas (ZAC), which have been heated to very high temperature during welding.
  • ZAC Heat Affected Areas
  • the carbon content must therefore be low, namely limited to 0.03% in order to obtain satisfactory resistance to intergranular corrosion as well as not to reduce formability.
  • the carbon content must satisfy a relationship with niobium, titanium and nitrogen, as will be explained later.
  • Manganese improves the adhesion of the oxide layer protecting the metal against corrosion, when its content is greater than 0.2%. However, above 1%, the hot oxidation kinetics become too fast and a less compact oxide layer develops, formed of spinel and chromin. The manganese content must therefore be contained between these two limits.
  • silicon is a very effective element in increasing resistance to oxidation during thermal cycling. To fulfill this role, a minimum content of 0.2% is necessary. However, in order not to decrease the hot-rolling and cold-forming ability, the silicon content should be limited to 1%.
  • Sulfur and phosphorus are unwanted impurities in large amounts because they decrease hot ductility and formability.
  • phosphorus easily segregates at grain boundaries and decreases their cohesion.
  • the sulfur and phosphorus contents must be respectively less than or equal to 0.01% and 0.04%.
  • Chromium is an essential element for the stabilization of the ferritic phase and for the increase of the resistance to oxidation.
  • its minimum content must be greater than or equal to 15% in order to obtain a ferritic structure at all temperatures of use and to obtain good resistance to water. 'oxidation. Its maximum content must not, however, exceed 22%, otherwise the mechanical strength at ambient temperature will increase excessively, which reduces the formability, or favoring embrittlement by demixing of the ferrite around 475 ° C.
  • Nickel is a gammagenic element which increases the ductility of steel. But in order to maintain a ferritic single-phase structure under all circumstances, its content must be less than or equal to 0.5%.
  • Molybdenum improves the resistance to pitting corrosion, but it decreases ductility and formability. This element is therefore not mandatory, and the content is limited to 2%.
  • Copper has a heat hardening effect which could be beneficial. Present in excessive quantity, however, it decreases the ductility during hot rolling and the weldability. As such, the copper content must therefore be less than or equal to 0.5%.
  • Aluminum is an important element of the invention. In fact, together or not with rare earths (REE), it improves the resistance to corrosion by urea if the formula Al + 30 x REE ⁇ 0.15% is observed, and if, moreover, a stabilization of the metal by titanium and niobium.
  • REE rare earths
  • Niobium and titanium are also important elements of the invention. Usually, these elements can be used as stabilizing elements in ferritic stainless steels. Indeed, the phenomenon of sensitization to intergranular corrosion by formation of chromium carbides, which was mentioned above, can be avoided by the addition of elements forming very thermally stable carbonitrides.
  • titanium and nitrogen combine even before the solidification of the liquid metal to form TiNs; and in the solid state at around 1100 ° C, titanium carbides and carbonitrides are formed.
  • the carbon and nitrogen present in solid solution in the metal are reduced as much as possible during its use.
  • Such a presence at excessively high levels would reduce the corrosion resistance of the metal and harden it.
  • a minimum Ti content of 0.16% is required.
  • the precipitation of TiN in the liquid metal is considered by steelmakers as a drawback in that it can lead to an accumulation of these precipitates on the walls of the nozzles of the pouring vessels (ladle, distributor continuous casting) which risks clogging these nozzles.
  • TiNs improve the structure which develops during solidification by helping to obtain an equiaxial rather than dendritic structure, and therefore improve the homogeneity of the final grain size.
  • the advantages of this precipitation outweigh its drawbacks, which can be minimized by choosing casting conditions which reduce the risks of the nozzles clogging.
  • Niobium combines with nitrogen and carbon in the solid state, and stabilizes the metal, just like titanium. Niobium therefore stably fixes carbon and nitrogen. But niobium also combines with iron to form in the range 550 ° C-950 ° C intermetallic compounds at grain boundaries, namely Fe 2 Nb Laves phases, which improves creep resistance in this range. temperature. A minimum content of 0.2% niobium is necessary to obtain this property. The conditions for obtaining this improvement in creep resistance are also strongly linked to the manufacturing process of the invention, in particular the annealing temperatures, and to an average grain size controlled and kept within the limits of 25 to 65 ⁇ m.
  • niobium and titanium it is also advisable to limit the additions of niobium and titanium.
  • the niobium and titanium contents is greater than 1% by weight, the hardening obtained is too great, the steel is less easily deformable and recrystallization after cold rolling is more difficult.
  • Zirconium would have a stabilizing role close to that of titanium, but is not deliberately used in the invention. Its content is less than 0.01%, and therefore must remain in the order of a residual impurity. An addition of Zr would be costly, and above all harmful, since zirconium carbonitrides, by virtue of their shape and their large size, greatly reduce the resilience of the metal.
  • Vanadium is a very inefficient stabilizer in the context of the invention given the low stability of vanadium carbonitrides at high temperature. On the other hand, it improves the ductility of the welds. However, at medium temperatures in a nitrogenous atmosphere it promotes nitriding of the metal surface by diffusion of nitrogen. The content is limited to 0.2%, taking into account the intended application.
  • nitrogen increases mechanical characteristics. However, nitrogen tends to precipitate at grain boundaries as nitrides, reducing corrosion resistance. In order to limit the problems of sensitization to intergranular corrosion, the nitrogen content must be less than or equal to 0.03%. In addition, the nitrogen content must satisfy the previous relationship between Ti, Nb, C and N. A minimum nitrogen of 0.009% is however necessary for the invention, because it guarantees the presence of TiN precipitates, and also the correct recrystallization of the cold-rolled strip during the final annealing operation, making it possible to obtain an average grain size of less than 65 microns. A content between 0.010% and 0.020%, for example 0.013%, may be recommended.
  • Cobalt is a hot-hardening element which degrades formability.
  • its content must be limited to 0.2% by weight.
  • the tin content should be less than or equal to 0.05%.
  • REE rare earths group together a collection of elements like cerium and lanthanum, among others, and are known to improve the adhesion of the layers of oxides which make steel resistant to corrosion. It has also been shown that rare earths improve resistance to intergranular corrosion by urea between 150 ° C and 700 ° C as in the case of aluminum already described, and respecting the Al + 30 x REE ⁇ relationship 0.15%. In synergy with aluminum and stabilizers, REEs help limit the diffusion of nitrogen. However, the rare earth content should not exceed 0.1%. Beyond this content, the production of the metal would be made difficult because of the reactions of the REEs with the refractories coating the ladle.
  • an annealing step can be added between the hot rolling and the cold rolling. This annealing takes place between 1000 and 1100 ° C for a period of 30 s to 6 min.
  • the cast samples were processed according to the following method.
  • the metal which is initially in the form of a 20mm thick larget, is brought to a temperature of 1200 ° C, and hot rolled in 6 passes to a thickness of 2 , 5 mm.
  • a first annealing of the hot-rolled strip can then be carried out at 1050 ° C. with the sample being maintained for 1 min 30 sec at this temperature.
  • n ° 1 to 11 and some reference examples (n ° 12 and 19) were treated with and without this first annealing, and it was possible to verify that they had, in both cases, properties very similar finals.
  • the execution of this first annealing makes it possible to obtain a slight improvement in formability, but for the attainment of the typical objectives of the invention, it is the conditions of the final annealing which are the only determining factors, in combination with the other essential characteristics. process and, of course, the composition of the steel.
  • Tables 2 and 3 correspond to those observed on the samples which have not undergone the first annealing of the variant which has just been described.
  • the metal After shot blasting and pickling, the metal is cold rolled at ambient temperature, ie approximately 20 ° C., in five passes, to a thickness of 1 mm.
  • the metal is annealed at 1050 ° C. with maintenance for 1 min 30 sec at this temperature, then it is pickled.
  • the sample is sprayed with a mixture containing 32.5% urea and 67.5% water (flow rate: 0.17ml / min), and simultaneously undergoes a thermal cycle between 200 and 600 ° C, with a triangular signal with period 120 sec as shown on the figure 1 by curve 1.
  • the temperature rise from 200 to 600 ° C lasts 40 sec, then cooling begins as soon as the temperature of 600 ° C is reached and continues up to 200 ° C for 80 sec.
  • Electrolytic copper plating of the sample is carried out, before coating, in a solution of CuSO 4 at 210 g / L and H 2 SO 4 at 30 ml / l; the imposed current density is 0.07 A / cm 2 for 5 minutes, then 0.14 A / cm2 for 1 minute. This procedure is considered optimal for obtaining good copper plating.
  • An electrolytic attack is carried out in a 5% solution of oxalic acid for 15s at 20 ° C.
  • the imposed current density is 60 mA / cm 2 .
  • This procedure B reveals two areas corroded by urea observed under the microscope at magnification x 1000.
  • the mechanical strength of the welds was evaluated using a tensile test at 300 ° C.
  • Two samples of the same cast are welded by the MIG / MAG process with a 430LNb wire under the following conditions: 98.5% argon, 1.5% oxygen, voltage: 26 V wire speed: 10m / min, current: 250 A, welding speed: 160 cm / min, energy: 2.5 kJ / cm (Welding procedure C). The result is judged all the more satisfactory when the ratio between the mechanical resistance for the welded specimen and for the non-welded specimen is close to 100%.
  • welds carried out on the castings according to the invention have mechanical strengths very comparable to those of the base metal, namely always greater than 80%.
  • the mechanical strength of the welds present in the components of the exhaust line, in particular when they are obtained by the MIG / MAG process, is therefore improved by the invention.
  • a minimum content of 0.2% of Nb is a condition for improving creep resistance and limiting the deformation of the parts during their use at high temperature.
  • Table 3 Depth of intergranular corrosion by urea and mechanical resistance of welds as a function of the average grain size of a sample Average grain size ( ⁇ m) Final annealing temperature (° C) Al + 30 * REE (%) Nb (%) 1 / [Nb + 7 / 4Ti-7 * (C + N)] Intergranular corrosion by urea, depth ( ⁇ m) Mechanical resistance of welds at 300 ° C (% compared to that of the base metal) 35 1070 0.207 0.4 2 3 90 5 900 0.207 0.4 2 11 90 200 1150 0.207 0.4 2 2 70
  • the grain size obtained on the product after the final annealing is a fundamental characteristic for simultaneously obtaining all the targeted properties.
  • a grain size that is too small (5 ⁇ m in the example cited) leads to intergranular corrosion by urea which extends over too great a depth.
  • Too large a grain size (200 ⁇ m in the example cited) makes it possible to maintain a sufficiently low sensitivity to intergranular corrosion, but it is then the mechanical strength of the welds which becomes unsatisfactory.

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Claims (7)

  1. Ferritisches Blech aus rostfreiem Stahl mit einer Zusammensetzung, ausgedrückt in Gewichtsprozenten, von:
    - Spuren ≤ C ≤ 0,03%,
    - 0,2% ≤ Mn ≤ 1%,
    - 0,2% ≤ Si ≤ 1%,
    - Spuren ≤ S ≤ 0,01%,
    - Spuren ≤ P ≤ 0,04%,
    - 15% ≤ Cr ≤ 22%,
    - Spuren ≤ Ni ≤ 0,5%,
    - Spuren ≤ Mo ≤ 2%,
    - Spuren ≤ Cu ≤ 0,5%,
    - 0,160% ≤ Ti ≤ 1%,
    - 0,02% ≤ Al ≤ 1%,
    - 0,2% ≤ Nb ≤ 1%,
    - Spuren ≤ V ≤ 0,2%,
    - 0,009% ≤ N ≤ 0,03%, vorzugsweise zwischen 0,010% und 0,020%,
    - Spuren ≤ Co ≤ 0,2%,
    - Spuren ≤ Sn ≤ 0,05%,
    - seltene Erden (REE) ≤ 0,1%,
    - Spuren ≤ Zr ≤ 0,01%,
    - wobei der Rest der Zusammensetzung aus Eisen und unvermeidbaren Verunreinigungen, welche aus der Erstellung resultieren, gebildet ist,
    - wobei die Gehalte von Al und von seltenen Erden (REE) den folgenden Zusammenhang erfüllen: Al + 30 × REE ≥ 0,15 % ,
    Figure imgb0008
    - wobei die Gehalte von Nb, C, N und Ti in % den folgenden Zusammenhang erfüllen: 1 / Nb + 7 / 4 × Ti − 7 × C + N ≤ 3 ,
    Figure imgb0009
     wobei das besagte Blech eine Struktur, welche vollständig rekristallisiert ist, und eine mittlere ferritische Korngröße, welche zwischen 25 und 65 µm liegt, hat.
  2. Verfahren zum Herstellen eines ferritischen Blechs aus rostfreiem Stahl, dadurch gekennzeichnet, dass:
    - man einen Stahl erstellt, welcher die Zusammensetzung gemäß Anspruch 1 hat,
    - man ein Halbprodukt ausgehend von diesem Stahl gießt,
    - man das Halbprodukt auf eine Temperatur von mehr als 1000°C und weniger als 1250°C bringt und man das Halbprodukt warmwalzt, um ein warmgewalztes Blech mit einer Dicke, welche zwischen 2,5 und 6 mm liegt, zu erhalten,
    - man das besagte warmgewalzte Blech kaltwalzt, bei einer Temperatur, welche zwischen der Umgebung und 300°C liegt, in einem einzigen Schritt oder in mehreren Schritten, welche durch Zwischentempervorgänge getrennt sind,
    - man einen finalen Tempervorgang des kaltgewalzten Blechs ausführt, bei einer Temperatur, welche zwischen 1000 und 1100°C liegt, und für eine Dauer, welche zwischen 10 Sekunden und 3 Minuten liegt, um eine vollständig rekristallisierte Struktur mit einer mittleren Korngröße, welche zwischen 25 und 65 µm liegt, zu erhalten.
  3. Verfahren zum Herstellen eines ferritischen rostfreien Blechs, dadurch gekennzeichnet, dass:
    - man einen Stahl erstellt, welcher die Zusammensetzung gemäß Anspruch 1 hat,
    - man ein Halbprodukt ausgehend von diesem Stahl gießt,
    - man das Halbprodukt auf eine Temperatur von mehr als 1000°C und weniger als 1250°C bringt und man das Halbprodukt warmwalzt, um ein warmgewalztes Blech mit einer Dicke, welche zwischen 2,5 und 6 mm liegt, zu erhalten,
    - man das warmgewalzte Blech bei einer Temperatur, welche zwischen 1000 und 1100°C liegt, und für eine Dauer, welche zwischen 30 Sekunden und 6 Minuten liegt, tempert,
    - man das besagte warmgewalzte Blech kaltwalzt bei einer Temperatur, welche niedriger als 300°C ist, in einem einzigen Schritt oder in mehreren Schritten, welche durch Zwischentempervorgänge getrennt sind,
    - man einen finalen Tempervorgang des kaltgewalzten Blechs ausführt, bei einer Temperatur, welche zwischen 1000 und 1100°C liegt, und für eine Dauer, welche zwischen 10 Sekunden und 3 Minuten liegt, um eine vollständig rekristallisierte Struktur mit einer mittleren Korngröße, welche zwischen 25 und 65 Mikrometern liegt, zu erhalten.
  4. Verfahren gemäß Anspruch 2 oder 3, dadurch gekennzeichnet, dass die Warmwalztemperatur von 1180 bis 1200°C ist.
  5. Verfahren gemäß einem der Ansprüche 2 bis 4, dadurch gekennzeichnet, dass die Temperatur des finalen Tempervorgangs zwischen 1050 und 1090°C liegt.
  6. Verwendung eines Blechs aus Stahl, welches mittels des Verfahrens gemäß einem der Ansprüche 2 bis 5 hergestellt ist, für die Herstellung von Teilen, welche eine Formgebung und ein Schweißen involvieren und welche dafür bestimmt sind, einer periodischen Verwendungstemperatur, welche zwischen 150°C und 700°C liegt, und einem Sprühen mit einer Mischung aus Wasser, aus Harnstoff und aus Ammoniak oder einem Sprühen mit Harnstoff oder mit Ammoniak ausgesetzt zu sein.
  7. Verwendung gemäß Anspruch 6, dadurch gekennzeichnet, dass die besagten Teile Teile von Abgasleitungen von Verbrennungsmotoren sind, welche mit einem Katalysatorsystem zur Reduktion von Stickoxiden mittels Einspritzens von Harnstoff oder von Ammoniak ausgestattet sind.
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HUE052513T2 (hu) 2021-05-28
US20160115562A1 (en) 2016-04-28
CA2883538C (fr) 2019-11-26
CN104903482B (zh) 2017-03-08
ES2831163T3 (es) 2021-06-07
KR20150099706A (ko) 2015-09-01
BR112015004633A2 (pt) 2017-07-04
WO2014033372A1 (fr) 2014-03-06
US9873924B2 (en) 2018-01-23
RU2603519C2 (ru) 2016-11-27
MX2015002716A (es) 2015-08-14
JP2015532681A (ja) 2015-11-12
IN2015DN01710A (de) 2015-05-22
CN104903482A (zh) 2015-09-09

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