EP0352597B1 - Procédé de fabrication de feuillard laminé à chaud ou tôles fortes - Google Patents

Procédé de fabrication de feuillard laminé à chaud ou tôles fortes Download PDF

Info

Publication number
EP0352597B1
EP0352597B1 EP89113109A EP89113109A EP0352597B1 EP 0352597 B1 EP0352597 B1 EP 0352597B1 EP 89113109 A EP89113109 A EP 89113109A EP 89113109 A EP89113109 A EP 89113109A EP 0352597 B1 EP0352597 B1 EP 0352597B1
Authority
EP
European Patent Office
Prior art keywords
max
product
slab
process according
deformation
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
Application number
EP89113109A
Other languages
German (de)
English (en)
Other versions
EP0352597A1 (fr
Inventor
Hans Dipl.-Ing. Dr. Pircher
Rudolf Dipl.-Ing. Kawalla
Jürgen Dipl.-Ing. Mahn
Walter Dipl.-Ing. Wilms
Waldemar Dipl.-Ing. Wolpert
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Thyssen Stahl AG
Original Assignee
Thyssen Stahl AG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Thyssen Stahl AG filed Critical Thyssen Stahl AG
Publication of EP0352597A1 publication Critical patent/EP0352597A1/fr
Application granted granted Critical
Publication of EP0352597B1 publication Critical patent/EP0352597B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/30—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process
    • B21B1/32—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work
    • B21B1/34—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a non-continuous process in reversing single stand mills, e.g. with intermediate storage reels for accumulating work by hot-rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • 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

Definitions

  • the invention relates to a method for producing hot strip or heavy plates from rustproof and heat-resistant molybdenum-containing steels or from molybdenum-containing wrought alloys based on nickel with a final thickness in the range from 5 to 60 mm by producing a slab from ingot casting or by continuous casting, heating the slab at one Temperature above 1,100 ° C, subsequent hot rolling of the slab and accelerated cooling of the product rolled to its final thickness.
  • a method according to the preamble of claim 1 for the production of austenitic stainless steel plates with high corrosion resistance and high mechanical strength both at ambient temperature and at high temperatures is known from DE-OS 36 17 907. It can be seen from this prior art document that the steel plates, i.e. Heavy plates made of rust-proof austenitic steels of the composition specified in the publication after the roughing and finishing rolling and the subsequent cooling in air to room temperature usually have to be subjected to a subsequent heat treatment or solution annealing. This is carried out so that the hardening caused by the deformation is broken down and precipitations of intermetallic or carbidic phases are dissolved, which negatively affect the corrosion resistance of the product.
  • the subsequent solution annealing must generally take place at temperatures of more than 1,000 ° C. and correspondingly long holding times which are sufficient to bring the precipitations back into solution.
  • the deformation-related solidification is reduced simultaneously as a result of recovery and recrystallization.
  • the stainless steel plates or heavy plates produced by this conventional method have in the solution-annealed state with regard to their mechanical properties, e.g. Strength and toughness, as well as corrosion resistance, a property profile for which a low mechanical strength is characteristic.
  • the solution annealing following the pre- and finish rolling and the subsequent cooling in air to room temperature means however, due to the reheating of the already rolled product to more than 1,000 ° C and the required holding times, high production costs and longer production times. Furthermore, this subsequent annealing process usually involves additional scaling of the product, which can cause its surface quality to deteriorate. As a rule, this means an additional effort for the required final scaling of the finished rolled product.
  • the product produced by this process has a much better mechanical and comparable corrosion resistance.
  • a higher strength is achieved in particular if the hot rolling also takes place in the non-recrystallization area.
  • the heating and heating temperature for the slab is preferably in the range from 1,100 to 1,200 ° C.
  • the finish-rolling temperature is in the range from 900 to Assumes 970 ° C, that is in any case less than 1,000 ° C and immediately after finish rolling with a temperature loss of only about 10 ° C the accelerated cooling begins, to a value of 500 ° C, preferably 300 ° C, in particular down to room temperature. Only when the final thickness of the product or heavy plate is 40 mm, in particular 100 mm, does a finish rolling temperature of more than 1,000 ° C result.
  • the finish-rolling temperature drops so much that a property profile comparable to that of heavy plates in solution-annealed condition, for example with regard to strength, toughness and corrosion resistance, cannot be set. Rather, the method known from DE-OS 36 17 907 basically gives a higher mechanical strength. However, if this is not desired with regard to the processing and use properties of the heavy plates, the finished rolled plates must then be subjected to a subsequent solution treatment, provided that they have a final thickness of less than 60 mm, in particular less than 40 mm.
  • hot strip and the heavy plates should have a property profile as in the solution-annealed condition, then heat treatment or solution annealing is still essential to break down the deformation-related hardening and to dissolve excretions.
  • hot strip and heavy plate with a final thickness of less than 60 mm are primarily affected, in particular those with a thickness in the range between 8 and 40 mm. Accordingly, if an increase in the strength properties is not desired, then with the method known from DE-OS 36 17 907 only heavy plates can be safely produced without subsequent solution treatment, which have a final thickness of more than 60 mm, but are rarely used in practice .
  • so far only the production of hot strip with a final thickness of less than about 8 or 10 mm has been possible without problems, which, however, has to be solution-annealed in any case after the finish rolling.
  • EP-OS 0 144 694 discloses a modified process for the production of flat, band-shaped or plate-shaped semi-finished products, for example with a final cross section of 15 mm ⁇ 40 mm, from a stainless austenitic or martensitic steel, but which provides solution annealing.
  • the workpiece made of stainless steel with the composition specified in the publication is first heated to a high temperature in the order of 1200 ° C. and heated through at this temperature. It is then pre-rolled and finish-rolled warm at a temperature in the range of 1,000 to 1,100 ° C in such a way that a sufficiently high deformation during the rolling process ensures complete recrystallization of the rolling stock.
  • solution annealing and subsequent quenching of the semi-finished product in water from this temperature range is carried out to almost room temperature.
  • An essential feature of this process is that the solution annealing immediately following the rolling process is carried out in a heat after the last or the last rolling pass and the workpiece is then quenched directly from the solution annealing temperature in water without any additional treatment.
  • this method provides for a roller heating system, which is intended to largely prevent premature and excessive cooling of the workpiece during rolling in order to prevent the finished workpiece from being reheated to the required solution solution and quenching temperature of more than 1,000 ° C.
  • this additional heating for the reheating of the finished rolled product and in particular the proposed roller heating would mean a considerable additional outlay in the production of hot strip or heavy plates, which was previously customary.
  • the invention has for its object to provide a method of the type mentioned, according to which products in the form of hot strip or heavy plates with the composition given in Table 1 are hot-rolled and have a property profile after accelerated cooling, for example with regard to strength, toughness and corrosion resistance , which corresponds to that of solution annealed hot strip or heavy plate.
  • this object is achieved in accordance with the measures specified in the characterizing part of claim 1 as follows: Initially, slabs are produced from ingot casting or by continuous casting from rustproof and heat-resistant steels or from wrought alloys based on nickel with the composition given in Table 1 and heated at a temperature of more than 1,100 ° C. before hot rolling. Immediately afterwards, the pre-rolling phase of the hot rolling of the heated slabs begins without interruptions to no less than 1/6 of their initial thickness, i.e. the slabs are reduced to as little as possible between the individual deformation passes in extreme cases to 1/6 of their initial thickness. Hot rolling is predominantly carried out with deformation stitches in which the degree of deformation per stitch in the thickness direction is greater than the degrees of deformation indicated by curve A in FIG.
  • the initial thickness of the slab or slabs is usually in the order of about 150 to 250 mm. If, however, the slabs produced by continuous casting have a thickness of less than about 50 mm or less, the reduction in the product in them can also be used according to the invention the first rolling phase.
  • the finishing rolling to the final thickness is then carried out according to measure ba) and bb) of claim 1 above a minimum temperature which is dependent on the molybdenum content of the product and which must not be undercut.
  • accelerated cooling takes place at the core without more than 100 s thereafter, at a speed of more than 3 K / s, preferably more than 5 K / s, except for a temperature equal to or less than 650 ° C.
  • hot strip and heavy plates made of the steels specified in Table 1 can be made to a final thickness in the range of 5 to 60 mm and with a property profile that corresponds to the mechanical properties and the corrosion resistance of solution-annealed hot strips and heavy plates.
  • the strips and sheets produced according to the invention have a more uniform, in particular very fine-grained and largely excretion-free structure, as a result of which their processing and use properties are improved.
  • thin strips and sheets with a preferred final thickness in the range from 8 to 40 mm can now be hot-rolled to the final thickness without additional heat input during the rolling out in such a way that subsequent solution annealing is no longer required .
  • the properties of the strips and sheets produced by the process according to the invention can be further improved and optimized by hot-rolling and the subsequent accelerated cooling in accordance with the measures specified in subclaims 2 to 6.
  • the method according to claim 3 relates to the production of hot strip and the method according to claim 4 to the production of heavy plates. If at the same time all the deformation stitches of the roughing phase have a degree of deformation which is greater than the degrees of deformation indicated by curve A in FIG. 1, hot strip and heavy plates can be e.g. Manufacture with optimal values in terms of strength, toughness and corrosion resistance.
  • the method according to the invention can preferably be applied to the production of hot strip and heavy plates from rustproof and heat-resistant steels with an analysis according to claims 7 to 10 and 13 to 16 as well as from a wrought nickel base alloy with the composition specified in claims 11 and 12. If the method is preferably applied to rustproof and heat-resistant austenitic steels with the composition according to claims 15 and 16, hot strip and / or heavy plates with high toughness and increased corrosion resistance are obtained, which afterwards as a finished product are easy to process with regard to hot forming, cold forming and welding have.
  • Table 1 shows the composition of those stainless and heat-resistant steels and wrought alloys based on nickel, from which hot strip and heavy plates can be produced by the process according to the invention.
  • the five different alloys specified in Table 3 were selected, from which hot strip with a final thickness of 10 and 15 mm and heavy plates with a final thickness in the range from 10 to 40 mm were produced by the process according to the invention.
  • These are two stainless austenitic steels with a molybdenum content of less than 1.0%, two further stainless austenitic steels with a molybdenum content of more than 1.0% and a nickel-based alloy with the composition given in Table 3.
  • preliminary slabs with a thickness in the range of 170 to 265 mm were first produced and then heated to a temperature of more than 1,100 ° C. and heated through at this temperature.
  • the hot strip and the heavy plates were then heated from them
  • the slabs were first rolled out to a final thickness in a pre-rolling phase and then in a subsequent finishing rolling phase, before the finished rolled product was accelerated to a temperature of less than 650 ° C. at a rate of more than 3 K / s.
  • the degrees of deformation per pass were selected both in the roughing phase and in the finish-rolling phase in accordance with the dependence of the degree of deformation on the surface or surface of the material to be rolled, which is shown in Table 2 and shown in FIG. 1.
  • Table 4 the hot rolling and cooling conditions, according to which the five different alloys for hot strip (W) and heavy plates shown in Table 3 were rolled out to final thickness, are given in Table 4.
  • Table 5 compares the results obtained from hot strip and heavy plate produced according to the invention, from solution-annealed and annealed and not annealed according to the invention.
  • Hot rolling in the recrystallization area and at high temperatures is not sufficient to set the properties desired for the hot strip and the heavy plates.
  • a homogeneous and fine-grained structure which is improved compared to the solution-annealed state can be set provided the hot rolling conditions in the finish-rolling phase for hot strip according to subclaims 2 and 3 and for heavy plates according to subclaims 2 and 4 can be set.
  • the hot rolling conditions in the finish rolling phase, in addition to measure bb), only feature ba) according to claim 1 a generally fine-grained structure is also generally achieved, but to a small extent also has coarse grain.
  • the hot strips and heavy plates produced according to the invention have comparable mechanical properties and corrosion resistance to the products in the solution-annealed state.
  • the exemplary embodiments according to the invention and the comparative examples in Tables 4 and 5 show that hot strip and heavy plates made of rustproof and heat-resistant steels or of wrought alloys based on nickel with the composition given in Table 1 with a final thickness in the range from 5 to 60 mm, preferably in the range from 8 to 40 mm, can be produced by the process according to the invention with a property profile which corresponds to the property profile of the corresponding strips and sheets in the solution-annealed state.
  • the strips and sheets produced according to the invention advantageously have a homogeneous and fine-grained structure that is largely free of excretions, which further improves their processing and use properties.
  • the method according to the invention now makes it possible, in particular, to produce hot strip with a final thickness greater than approximately 5 mm in a simple and inexpensive manner by controlled hot rolling with subsequent accelerated cooling without the need for subsequent solution annealing.
  • Table 1 Stainless and heat-resistant steels Wrought alloys based on Ni ferritic and martensitic austenitic / ferritic austenitic Alloy element Alloy content in mass% Konlenstoff ⁇ 0.35 ⁇ 0.05 ⁇ 0.15 ⁇ 0.1 manganese ⁇ 2.5 ⁇ 10.0 ⁇ 20.0 ⁇ 4.0 silicon ⁇ 1.5 ⁇ 1.5 ⁇ 4.0 ⁇ 4.0 nickel ⁇ 3.0 4 - 7 ⁇ 35 (Rest Ni) chrome 6 - 30.0 10 - 30.0 10 - 30.0 10 - 30 molybdenum ⁇ 3.0 ⁇ 5.0 ⁇ 7.0 ⁇ 10 titanium ⁇ 1.5 ⁇ 1.5 ⁇ 1.5 Tantalum and / or niobium ⁇ 1.5 ⁇ 1.5 ⁇ 1.5 ⁇ 1.5

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Claims (17)

  1. Procédé de fabrication de feuillard laminé à chaud ou de tôle forte d'une épaisseur finale comprise entre 5 et 60 mm à partir d'acier inoxydable et résistant à la chaleur contenant du molybdène ou à partir d'un alliage corroyé à base de nickel contenant du molybdène par préparation d'un lingot à partir d'une coulée de lingots ou par coulée continue, chauffage du lingot à une température au-dessus de 1100 °C, puis laminage ä chaud du lingot et refroidissement rapide du produit laminé jusqu'à l'épaisseur finale, dans lequel
    a) le lingot réchauffé d'une épaisseur initiale supérieure à environ 50 mm est d'abord laminé jusqu'à une épaisseur non inférieure au 1/6 de l'épaisseur initiale, en majorité à l'aide de passes de déformation, de sorte que le degré de déformation par passe dans la direction de l'épaisseur est supérieur à celui représenté par la courbe A de la Fig. 1 qui est fonction de la température de surface du produit,
    ba) le lingot laminé dans un premier temps jusqu'à une une épaisseur inférieure au 1/6 de son épaisseur initiale ou un lingot réchauffé d'une épaisseur initiale inférieure à environ 50 mm, préparé par coulée continue, est ensuite laminé jusqu'à l'épaisseur finale en majorité à l'aide de passes de déformation, de sorte que le degré de déformation par passe dans la direction de l'épaisseur est supérieur à celui représenté par la courbe B1 de la Fig. 1 pour des temps de poses inférieurs à 10 secondes par la courbe B2 de la Fig. 1 pour des temps de poses supérieurs à 10 secondes, les degrés de déformation étant fonction de la température de surface du produit et du temps de pose entre deux passes successives.
    bb) par lequel la température de surface du produit fini laminé
    - n'est pas inférieure à 1030°C, dans la mesure où le produit contient jusqu'à 1,0% de molybdène et
    - n'est pas inférieure à 1050°c, dans la mesure où le produit contient plus de 1,0% de molybdène
    ou par lequel - dans la mesure où le produit fini laminé est constitué d'acier ferritique ou martensitique inoxydable et résistant à la chaleur - la température de surface du produit fini laminé
    - n'est pas inférieure à 980°C, dans la mesure où le produit contient jusqu'à 1,0% de molybdène et
    - n'est pas inférieure à 1000°C, dans la mesure où le produit contient plus de 1,0% de molybdène,
    c) le produit sans recuit de mise en solution est refroidi très rapidement au plus tard 100 secondes après la fin du laminage à une vitesse de plus 3 K/s au centre, de préférence de plus de 5 K/s, jusqu'à une température qui est inférieure ou égale à 650°C.
  2. Procédé selon la revendication 1, caractérisé en ce que toutes les passes de déformation avec lesquelles le lingot réchauffé est tout d'abord laminé jusqu'à une épaisseur inférieure au 1/6 de l'épaisseur initiale sont réalisées avec un degré de déformation qui est supérieur à'celui représenté par la courbe A de la Fig. 1 qui est fonction de la température de surface du produit.
  3. Procédé selon l'une des revendications 1 ou 2, caractérisé en ce qu'au moins 2/3 des passes de déformation avec lesquelles le produit est laminé jusqu'à son épaisseur finale sont réalisées avec un degré de déformation qui est supérieur à celui représenté par la courbe B1 de la Fig. 1 qui est fonction de la température de surface du produit et du temps de pose entre deux passes successives.
  4. Procédé selon l'une des revendications 1 ou 2, caractérisé en ce qu'au moins 3/4 des passes de déformation avec lesquelles le produit est laminé jusqu'à son épaisseur finale sont réalisées avec un degré de déformation qui est supérieur à celui représenté par la courbe B2 de la Fig. 1 qui est fonction de la température de surface du produit et du temps de pose entre deux passes successives.
  5. Procédé selon l'une des revendications 1 à 4, caractérisé en ce que, concernant la vitesse rapide de refroidissement, le produit fini laminé est lentement refroidi à l'air jusqu'à la température ambiante.
  6. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que dans la mesure où le produit fini laminé est constitué d'acier ferritique, martensétique ou austénitique-ferritique inoxydable et résistant à la chaleur, le produit final laminé refroidit rapidement à une température inférieure ou égale à 400°C.
  7. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que le lingot est préparé à partir d'un acier ferritique ou martensitique inoxydable et résistant à la chaleur constitué d'au plus 0,35% de C, d'au plus 2,5% de Mn, d'au plus 1,5%,de Si, d'au plus 3,0% de Ni, de 6,0 jusqu'à 30,0% de Cr, d'au plus 3,0% de Mo le restant représentant le fer et les impuretés inévitables.
  8. Procédé selon la revendication 7, caractérisé en ce que l'on ajoute en outre à l'acier ferritique ou martensitique inoxydable et résistant à la chaleur, un à un ou en combinaison, au plus 1,5% de Ti, au plus 1,5% de Ta et/ou Nb, au plus 1,5% de Al, au plus 0,5% de N, au plus 0,5% de V, au plus 0,5% de S.
  9. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que le lingot est préparé à partir d'un acier austénitique-ferritique inoxydable et résistant à la chaleur, constitué au plus de 0,05% de C, au plus 10,0% de Mn, au plus 1,5% de Si, de 4,0 jusqu'à 7,0% de Ni, de 10,0 jusqu'à 30,0% de Cr, au plus 5,0% de Mo, le restant représentant le fer et les impuretés inévitables.
  10. Procédé selon la revendication 9, caractérise en ce qu'on ajoute en outre à l'acier austénitique-ferritique inoxydable et résistant à la chaleur, un à un ou en combinaison, au plus 1,5% de Ti, au plus 1,5% de Ta et/ou Nb, au plus 5,0% de Cu, au plus 0,5% de Al, au plus 0,5% de N.
  11. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que le lingot est préparé à partir d'un alliage corroyé à base de nickel constitué d'au plus 0,1% de C, au plus 4,0% de Mn, au plus 4,0% de Si, de 10,0 jusqu'à 30,0 % de Cr, au plus 10,0% de Mo le restant représentant le fer et les impuretés inévitables.
  12. Procédé selon la revendication 11, caractérisé en ce qu'on ajoute en outre à l'alliage corroyé à base de nickel, un à un ou en combinaison, au plus 1,5% de Ti, au plus 1,5% et/ou Nb, au plus 5,0% de Cu, au plus 0,5% de Al, au plus 0,5% de N, au plus 45,0% de Fe.
  13. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que le lingot est préparé à partir d'un acier austénitique inoxydable et résistant à la chaleur constitué au plus de 0,15% de C, au plus de 20,0% de Mn, au plus 4,0% de Si, au plus 35,0% de Ni, de 10,0 jusqu'a' 30% de Cr, au plus 7,0% de Mo, le restant représentant le fer et les impuretés inévitables.
  14. Procédé selon la revendication 13, caractérisé en ce que l'on ajoute en outre à l'acier austénitique inoxydable et résistant à la chaleur, un à un ou en combinaison, au plus 1,5% de Ti, au plus 1,5% de Ta et/ou Nb, au plus 5,0% de Cu, au plus 1,0% de Al, au 0,5% de N, au plus 1,0%, de V, au plus 0,3% de S.
  15. Procédé selon l'une des revendications 13 ou 14, caractérisé en ce que le lingot est préparé à partir d'un acier austénitique inoxydable et résistant à la chaleur comprenant au maximum 3,0% de Si, de 7,0 jusqu'à 35,0% de Ni, au plus 0,5% de Al, au plus 0,035% de S.
  16. Procédé selon la revendication 15, caractérisé en ce que l'acier austénitique inoxydable et résistant à la chaleur est mélangé à de 7,0 jusqu'à 20% de Ni, de 15,0 jusqu'à 25,0 % de Cr, au plus de 5,0% de Mo.
  17. Procédé selon la revendication 16, caractérisé en ce que la teneur en ferrite-Delta de l'acier austénitique inoxydable et résistant à la chaleur utilisé est ajustée à une valeur inférieure à 10%, de préférence en contrölant les quantités ajoutées à l'acier des constituants d'alliages que sont le Ni, le N, le Mn et/ou le Cu.
EP89113109A 1988-07-28 1989-07-18 Procédé de fabrication de feuillard laminé à chaud ou tôles fortes Expired - Lifetime EP0352597B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3825634A DE3825634C2 (de) 1988-07-28 1988-07-28 Verfahren zur Erzeugung von Warmbad oder Grobblechen
DE3825634 1988-07-28

Publications (2)

Publication Number Publication Date
EP0352597A1 EP0352597A1 (fr) 1990-01-31
EP0352597B1 true EP0352597B1 (fr) 1994-06-22

Family

ID=6359745

Family Applications (1)

Application Number Title Priority Date Filing Date
EP89113109A Expired - Lifetime EP0352597B1 (fr) 1988-07-28 1989-07-18 Procédé de fabrication de feuillard laminé à chaud ou tôles fortes

Country Status (8)

Country Link
US (1) US4994118A (fr)
EP (1) EP0352597B1 (fr)
JP (1) JPH02175816A (fr)
KR (1) KR900001424A (fr)
AT (1) ATE107708T1 (fr)
CA (1) CA1318838C (fr)
DE (2) DE3825634C2 (fr)
ES (1) ES2058410T3 (fr)

Families Citing this family (25)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0688125A (ja) * 1992-09-09 1994-03-29 Aichi Steel Works Ltd 連続鋳造片及び鋼塊の熱間加工法
WO1995013404A1 (fr) * 1993-11-09 1995-05-18 Nisshin Steel Co., Ltd. Acier inoxydable possedant une excellente resistance a la corrosion causee par du sel fondu et procede de production dudit acier
KR0169172B1 (ko) * 1994-02-15 1999-01-15 아키모토 유우미 철-크롬계 합금
KR100334253B1 (ko) * 1999-11-22 2002-05-02 장인순 고온 용융염에서 내부식성이 우수한 합금강
JP4774633B2 (ja) * 2001-06-04 2011-09-14 大同特殊鋼株式会社 マルテンサイト系耐熱鋼の製造方法
DE10215597A1 (de) * 2002-04-10 2003-10-30 Thyssenkrupp Nirosta Gmbh Verfahren zum Herstellen eines hohe Kohlenstoffgehalte aufweisenden martensitischen Stahlbands und Verwendung eines solchen Stahlbands
DE10215598A1 (de) * 2002-04-10 2003-10-30 Thyssenkrupp Nirosta Gmbh Nichtrostender Stahl, Verfahren zum Herstellen von spannungsrißfreien Formteilen und Formteil
JP4883546B2 (ja) * 2002-09-20 2012-02-22 Ｊｘ日鉱日石金属株式会社 タンタルスパッタリングターゲットの製造方法
JP4263900B2 (ja) * 2002-11-13 2009-05-13 日鉱金属株式会社 Ｔａスパッタリングターゲット及びその製造方法
KR100698745B1 (ko) * 2003-04-01 2007-03-23 닛코킨조쿠 가부시키가이샤 탄탈륨 스퍼터링 타겟트 및 그 제조방법
US7892367B2 (en) * 2003-11-06 2011-02-22 Jx Nippon Mining & Metals Corporation Tantalum sputtering target
EP1876258A4 (fr) * 2005-04-28 2008-08-13 Nippon Mining Co Cible de pulverisation
US20060275168A1 (en) * 2005-06-03 2006-12-07 Ati Properties, Inc. Austenitic stainless steel
SE529003E (sv) 2005-07-01 2011-10-11 Sandvik Intellectual Property Ni-Cr-Fe-legering för högtemperaturanvändning
US8425696B2 (en) * 2005-10-04 2013-04-23 Jx Nippon Mining & Metals Corporation Sputtering target
JP4943219B2 (ja) * 2007-04-26 2012-05-30 山陽特殊製鋼株式会社 高強度で熱間加工性が良好なＭｏ、Ｔｉ含有オーステナイト系ステンレス鋼
CN101348888A (zh) * 2007-07-18 2009-01-21 青岛三庆金属有限公司 低镍奥氏体不锈钢及其制备方法
DE102007060133A1 (de) * 2007-12-13 2009-06-18 Witzenmann Gmbh Leitungsteil aus nickelarmem Stahl für eine Abgasanlage
EP3390679B1 (fr) 2015-12-14 2022-07-13 Swagelok Company Pièces forgées en acier inoxydable fortement allié sans hypertrempe
DE102016109253A1 (de) * 2016-05-19 2017-12-07 Böhler Edelstahl GmbH & Co KG Verfahren zum Herstellen eines Stahlwerkstoffs und Stahlwerksstoff
CN111041179B (zh) * 2019-12-03 2021-12-14 马鞍山钢铁股份有限公司 一种消除高Cr当量P92耐热钢高温铁素体的方法及高Cr当量P92耐热钢的制备方法
RU2735777C1 (ru) * 2020-05-07 2020-11-09 Федеральное государственное автономное образовательное учреждение высшего образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") Способ получения катаных полуфабрикатов из аустенитной коррозионностойкой стали
ES2953325T3 (es) * 2020-09-24 2023-11-10 Primetals Technologies Austria GmbH Instalación de laminación de compuestos de fundición y procedimiento para operar la instalación de laminación de compuestos de fundición
CN112496037B (zh) * 2020-11-16 2021-11-23 太原钢铁(集团)有限公司 一种镍基合金板材轧制方法
CN114178314B (zh) * 2021-12-09 2023-04-25 福建三宝钢铁有限公司 一种低合金高强度热轧卷板q390c轧制工艺

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4256516A (en) * 1978-12-26 1981-03-17 Nippon Kokan Kabushiki Kaisha Method of manufacturing non-magnetic Fe-Mn steels having low thermal expansion coefficients and high yield points
US4360391A (en) * 1981-05-22 1982-11-23 Nisshin Steel Co., Ltd. Process for production of coil of hot rolled strip of austenitic stainless steel
GB2115834B (en) * 1982-03-02 1985-11-20 British Steel Corp Non-magnetic austenitic alloy steels
JPS6026619A (ja) * 1983-07-22 1985-02-09 Nippon Kokan Kk <Nkk> オ−ステナイト系ステンレス厚鋼板の製造方法
DE3339593A1 (de) * 1983-11-02 1985-05-15 Brown, Boveri & Cie Ag, 6800 Mannheim Verfahren zur herstellung von halbzeug aus einem rostfreien austenitischen oder martensitischen stahl
JPS61272317A (ja) * 1985-05-29 1986-12-02 Nippon Kokan Kk <Nkk> 耐食性に優れた常温および高温域での高強度オ−ステナイト・ステンレス鋼材の製造方法
JPS6256530A (ja) * 1985-09-04 1987-03-12 Sumitomo Metal Ind Ltd 大径溶接鋼管用鋼板の製造方法
JPS63186822A (ja) * 1987-01-29 1988-08-02 Nkk Corp 高強度オ−ステナイト系ステンレス鋼の製造方法

Also Published As

Publication number Publication date
CA1318838C (fr) 1993-06-08
ES2058410T3 (es) 1994-11-01
DE58907934D1 (de) 1994-07-28
DE3825634A1 (de) 1990-02-01
EP0352597A1 (fr) 1990-01-31
KR900001424A (ko) 1990-02-27
US4994118A (en) 1991-02-19
DE3825634C2 (de) 1994-06-30
JPH02175816A (ja) 1990-07-09
ATE107708T1 (de) 1994-07-15

Similar Documents

Publication Publication Date Title
EP0352597B1 (fr) Procédé de fabrication de feuillard laminé à chaud ou tôles fortes
EP2366035B1 (fr) Feuillard d&#39;acier au manganèse à teneur accrue en phosphore et son procédé de fabrication
DE60127879T2 (de) Hochfestes warmgewalztes Stahlblech mit ausgezeichneten Reckalterungseigenschaften
DE60110586T2 (de) Kaltgewalztes stahlblech mit ausgezeichneten reckalterungseigenschaftenund herstellungsverfahren für ein solches stahlblech
DE60214086T2 (de) Hochduktiles Stahlblech mit exzellenter Pressbarkeit und Härtbarkeit durch Verformungsalterung sowie Verfahren zu dessen Herstellung
EP3655560B1 (fr) Produit plat en acier possédant une bonne résistance au vieillissement et son procédé de fabrication
EP2690183B1 (fr) Produit plat en acier laminé à chaud et son procédé de fabrication
EP1918406B1 (fr) Procédé pour la fabrication de produits plats à partir d&#39;un acier à plusieurs phases micro-allié en bore
EP1918402B1 (fr) Procédé de fabrication de produits plats en acier à partir d&#39;un acier formant une structure de phases complexes
EP0320773A2 (fr) Procédé pour la fabrication de tôles d&#39;acier plaqués, laminés à chaud
EP1918403B1 (fr) Procédé de fabrication de produits plats en acier à partir d&#39;un acier formant une structure marténsitique
DE3851374T2 (de) Kaltgewalzte Stahlbleche mit verbesserter Punktschweissfähigkeit und Verfahren zu ihrer Herstellung.
DE3401406A1 (de) Verfahren zur herstellung von stahlplatten mit hoher zugfestigkeit
EP2905348B1 (fr) Produit en acier plat de haute résistance avec une structure bainitique-martensitique et procédé de fabrication d&#39;un tel produit acier plat
EP2840159B1 (fr) Procédé destiné à la fabrication d&#39;un composant en acier
DE102018132860A1 (de) Verfahren zur Herstellung von konventionell warmgewalzten, profilierten Warmbanderzeugnissen
EP1918405B1 (fr) Procédé pour la fabrication de produits plats à partir d&#39;un acier à plusieurs phases allié en silice
DE3440752C2 (fr)
DE3881002T2 (de) Durch wärmrbehandlung härtbares warmgewalztes stahlfeinblech mit ausgezeichneter kaltverformbarkeit und verfahren zu seiner herstellung.
EP1398390B1 (fr) Acier ferritique-martensitique possédant une resistance élevée ayant une fine microstructure
DE102018132908A1 (de) Verfahren zur Herstellung von thermo-mechanisch hergestellten Warmbanderzeugnissen
DE10130774C1 (de) Verfahren zum Herstellen von hochfesten, aus einem Warmband kaltverformten Stahlprodukten mit guter Dehnbarkeit
EP1453984B1 (fr) Procede de production de feuillards ou de toles a chaud en acier microallie
EP1918404B1 (fr) Procédé pour la fabrication de produits plats à partir d&#39;un acier à plusieurs phases allié en aluminium
WO2008006346A2 (fr) Procédé de fabrication d&#39;un demi-produit en tôle adapté pour le formage à chaud

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: A1

Designated state(s): AT BE DE ES FR GB IT LU NL SE

17P Request for examination filed

Effective date: 19900626

17Q First examination report despatched

Effective date: 19920511

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE DE ES FR GB IT LU NL SE

REF Corresponds to:

Ref document number: 107708

Country of ref document: AT

Date of ref document: 19940715

Kind code of ref document: T

GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

Effective date: 19940628

REF Corresponds to:

Ref document number: 58907934

Country of ref document: DE

Date of ref document: 19940728

EPTA Lu: last paid annual fee
ET Fr: translation filed
ITF It: translation for a ep patent filed

Owner name: SOCIETA' ITALIANA BREVETTI S.P.A.

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2058410

Country of ref document: ES

Kind code of ref document: T3

EAL Se: european patent in force in sweden

Ref document number: 89113109.6

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
REG Reference to a national code

Ref country code: GB

Ref legal event code: IF02

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20030630

Year of fee payment: 15

Ref country code: LU

Payment date: 20030630

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20030703

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20030704

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20030708

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20030710

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20030711

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: ES

Payment date: 20030717

Year of fee payment: 15

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 20030724

Year of fee payment: 15

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040718

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040718

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040718

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040719

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040719

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20040731

BERE Be: lapsed

Owner name: *THYSSEN STAHL A.G.

Effective date: 20040731

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20050201

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20050201

EUG Se: european patent has lapsed
GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20040718

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20050331

NLV4 Nl: lapsed or anulled due to non-payment of the annual fee

Effective date: 20050201

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: 20050718

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20040719

BERE Be: lapsed

Owner name: *THYSSEN STAHL A.G.

Effective date: 20040731