EP0881305A1 - Procédé de fabrication de bandes minces d'acier inoxydable ferritique, et bandes minces ainsi obtenues - Google Patents
Procédé de fabrication de bandes minces d'acier inoxydable ferritique, et bandes minces ainsi obtenues Download PDFInfo
- Publication number
- EP0881305A1 EP0881305A1 EP98401090A EP98401090A EP0881305A1 EP 0881305 A1 EP0881305 A1 EP 0881305A1 EP 98401090 A EP98401090 A EP 98401090A EP 98401090 A EP98401090 A EP 98401090A EP 0881305 A1 EP0881305 A1 EP 0881305A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- strip
- temperature
- carbides
- cooling
- stainless steel
- 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.)
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Classifications
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- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/124—Accessories for subsequent treating or working cast stock in situ for cooling
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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
-
- 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
- C21D8/0221—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
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the invention relates to the metallurgy of stainless steels. More specifically, it concerns the casting of ferritic stainless steels directly from liquid metal in the form of strips a few mm thick.
- JP-A-62247029 which recommends a in-line cooling at a speed greater than or equal to 300 ° C / s between 1200 and 1000 ° C, followed by the winding which is carried out between 1000 and 700 ° C.
- the object of the invention is to propose an economical mode of production of thin strips of ferritic stainless steel of type AISI 430 and related by casting between cylinders, which gives said strips sufficient ductility to allow operations of unwinding, shearing of the edges and cold processing (pickling, rolling ...) of occur without incidents such as tape breakage or the appearance of cracks on the banks.
- this process should not include steps requiring the addition of complex facilities to a casting machine between standard cylinders.
- the invention consists, starting from a steel strip ferritic stainless steel of standard composition cast between cylinders, to cool and to wind said strip under special conditions, before subjecting it to a closed annealing.
- This treatment essentially aims to limit the formation of large carbides as much as possible weakeners. For that, it is necessary to limit the precipitation of carbides and to favor the transformation of austenite into martensite in the raw pouring stage, avoiding however that this transformation into martensite does not occur when the strip is not yet wound.
- Treatment A consists, in accordance with the prior art described above, of allow the strip to cool naturally in the open air after it leaves the casting cylinders, and wind it at around 800 ° C, while it is in the area of precipitation of chromium carbides at ferritic joints and at ferrite-austenite interfaces. This winding causes, as we said, a considerable slowing down of the cooling of the band, which is then forced to stay long in the area of transformation of austenite into ferrite and chromium carbides, before ending up at ambient temperature.
- Treatment C representative of the invention, consists in first leaving the strip to cool naturally, without being coiled, so that it does not stay in the area transforming austenite into ferrite and chromium carbides, and not winding only at a temperature of approximately 600 ° C. During the cooling of the strip wound, this ends up substantially joining the final thermal path of treatment A.
- Treatment D is in principle identical to treatment C, but the winding of the strip takes place only at a temperature of 300 ° C approximately. This temperature remains imperatively higher than Ms (which depends on the chemical composition of the steel), and during the cooling of the coil we prevent the band from staying in the area where the martensitic transformation would take place very importantly. Its final thermal path joins those of treatments A and C.
- the snapshot in Figure 2 shows a portion of a sample of a strip of reference which followed the thermal path A of FIG. 1 (therefore a winding at 800 ° C) for be brought in coiled form at room temperature, then undergone closed cup annealing under usual conditions, namely a stay at approximately 800 ° C. for 6 hours.
- the strip has the chemical composition specified above and a thickness of 3 mm.
- Zones 4 comprising small ferritic grains resulting from the transformation of martensite ⁇ 'during the closed annealing represents only a minority fraction of the sample.
- the winding temperature has no influence on the ductility at 20 ° C. of the raw casting strip, which has not yet undergone closed annealing.
- This ductility is very poor, and it is not improved by closed cup annealing in the case of the reference strip, hot wound.
- the closed cup annealing in this reference case was powerless to promote a structure of the metal matrix and a distribution of carbides favorable to good ductility.
- the ductility of the wound strip under the conditions recommended by the invention could be considerably improved by closed cup annealing, and brought to a very satisfactory level.
- a resilience of the order of 30 to 40 J / cm 2 is sufficient so that cold treatments (unwinding, shearing of the edges in particular) can be carried out without damage to the strip.
- the first fundamental idea of the invention is to impose on the band leaving the cylinders a cooling path which makes it possible to limit the precipitation carbides, especially avoiding those which could come from the decomposition of austenite and which could coalesce into large continuous films during vase annealing closed.
- the second idea is to promote, at the same stage of development, the transformation from austenite to martensite so as to obtain as much fine-grained ferrite as possible during closed annealing. These conditions are met if we limit the time spent by the strip cast in the precipitation range of carbides and nitrides from ferrite, and especially if it is avoided to stay in the field of the transformation of austenite in ferrite and carbides.
- the temperature is initially between ambient and 200 ° C. It is typically performed at a temperature of 800-850 ° C for at least 4 hours.
- the process according to the invention has the advantage of not requiring any particular and costly adaptations of the shade such as the incorporation of stabilizers and / or the lowering of carbon and nitrogen contents to unusually low levels. It can be run on a casting machine continuous between cylinders which does not need to be fitted with a rolling mill hot strip coming out of the cylinders. Nor does it require adaptations specific stages of the manufacturing cycle after casting (closed cup annealing, shearing of banks, stripping ). The only modification to a casting installation between standard cylinders that its installation is likely to require is the possible addition of a belt cooling device under the cylinders.
- Such a device which could be very simple design, would ensure that the tape never stays in the area of transformation of austenite into ferrite and carbides and that the winding takes place always at 600 ° C or less, whatever the casting speed and the thickness of the strip, and even if the winder is located relatively close to the rolls (which can be a contrario desirable for the casting of other types of steels).
- This composition corresponds to a ⁇ p criterion of 46.5% and at a temperature Ac1 826 ° C.
- a winding carried out at 500 ° C. provides the strip with energy absorbed at 20 ° C. (after closed cup annealing) of 160 J / cm 2 , for conditions of test similar to those of the tests in table 1 above.
- the winding is carried out at 800 ° C, the energy absorbed at 20 ° C is only 100 J / cm 2 .
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Catalysts (AREA)
- Artificial Fish Reefs (AREA)
- Metal Rolling (AREA)
- Wrappers (AREA)
- Heat Treatment Of Steel (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
Description
- la bande brute de coulée présente essentiellement une structure colonnaire à gros grains ferritiques (la taille moyenne du grain est supérieure à 300 µm dans l'épaisseur de la bande), qui est une conséquence directe de la succession d'une solidification rapide sur les cylindres et d'un séjour de la bande à haute température après qu'elle a quitté les cylindres, lorsqu'elle ne subit pas de refroidissement forcé :
- les grains ferritiques présentent une dureté élevée, due à leur sursaturation en éléments interstitiels (carbone et azote) ;
- la présence de martensite issue de la trempe de l'austénite présente à haute température.
- des élaborations coûteuses et difficiles du métal liquide destiné à la coulée de la bande, si on veut obtenir les basses teneurs en carbone et azote nécessaires, voire le cas échéant les teneurs souhaitées en éléments stabilisants ;
- des traitements thermiques et thermomécaniques effectués sur la ligne de coulée au moyen d'installations lourdes (laminoir à chaud en ligne) ;
- et la réalisation de cycles thermiques complexes nécessitant également des installations spécialement adaptées pour obtenir les vitesses de refroidissement élevées ou les temps de maintien à haute température nécessaires.
- la figure 1 qui situe sur un diagramme montrant les courbes de transformation au refroidissement de la nuance AISI 430 quatre exemples A, B, C, D de chemins thermiques suivis par la bande après sa sortie des cylindres de coulée, dont deux exemples C, D où elle subit un traitement selon l'invention ;
- la figure 2 qui montre un cliché en microscopie électronique en transmission sur lame mince d'une bande ayant suivi le chemin thermique A de la figure 1, puis un recuit vase clos ;
- la figure 3 qui montre un cliché en microscopie électronique en transmission sur lame mince d'une bande ayant, selon l'invention, suivi un chemin thermique intermédiaire entre les chemins C et D de la figure 1, puis un recuit vase clos.
- carbone : 0,043% ;
- silicium : 0,24% ;
- soufre : 0,001% ;
- phosphore : 0,023% ;
- manganèse : 0,41% ;
- chrome : 16,36% ;
- nickel : 0,22% ;
- molybdène : 0,043% ;
- titane : 0,002% ;
- niobium : 0,004% ;
- cuivre : 0,042% ;
- aluminium : 0,002% ;
- vanadium : 0,064% ;
- azote : 0,033% ;
- oxygène : 0,0057% ;
- bore : moins de 0,001% ;
- carbone: 0,040% ;
- silicium: 0,23% ;
- soufre: 0,001% ;
- phosphore: 0,024% ;
- manganèse: 0,40% ;
- chrome: 16,50% ;
- nickel: 0,57% ;
- molybdène: 0,030% ;
- titane: 0,002% ;
- niobium: 0,001% ;
- cuivre: 0,060% ;
- aluminium: 0,003% ;
- vanadium: 0,060% ;
- azote: 0,042% ;
- oxygène: 0,0090% ;
- bore: moins de 0,001%.
- une structure colonnaire à gros grains ferritiques coexistant avec de nombreuses zones à petits grains ferritiques parsemés de carbures ;
- l'absence de films continus de gros carbures, remplacés par des chapelets de petits carbures discontinus, présents aux frontières entre les gros grains ferritiques et les zones à petits grains ferritiques ;
- dans le cas, selon la version de base de l
- et, généralement, l'absence de teneurs significatives en éléments stabilisants tels que le niobium, le vanadium, le titane, l'aluminium, le molybdène ; comme on l'a dit, de tels éléments peuvent éventuellement être présents pour diverses raisons, mais ils n'exercent pas d'influence notable sur la ductilité de la bande.
Claims (6)
- Procédé de fabrication de bandes minces d'acier inoxydable ferritique d'épaisseur inférieure à 10 mm, selon lequel, directement à partir de métal liquide, on solidifie entre deux cylindres rapprochés à axes horizontaux, refroidis intérieurement et tournant en sens contraires, une bande d'un acier inoxydable ferritique du type contenant au plus 0,012% de carbone, au plus 1% de manganèse, au plus 1% de silicium, au plus 0,040% de phosphore, au plus 0,030% de soufre et entre 16 et 18% de chrome, caractérisé en ce qu'on refroidit ou on laisse se refroidir ensuite ladite bande en évitant de la faire séjourner dans le domaine de transformation de l'austénite en ferrite et carbures, en ce qu'on effectue le bobinage de ladite bande à une température comprise entre 600°C et la température de transformation martensitique Ms, en ce qu'on laisse la bande bobinée se refroidir à une vitesse maximale de 300°C/h jusqu'à une température comprise entre 200°C et la température ambiante, et en ce qu'on procède ensuite à un recuit vase clos de ladite bande.
- Procédé selon la revendication 1, caractérisé en ce que ledit recuit vase clos est réalisé à une température de 800 à 850°C pendant au moins 4 heures.
- Procédé selon la revendication 1 ou 2, caractérisé en ce qu'on évite de faire séjourner la bande dans le domaine de transformation de l'austénite en ferrite et carbures en lui conférant une vitesse de refroidissement supérieure ou égale à 10°C/s au moins entre le moment où la bande solidifiée quitte les cylindres et le moment où elle atteint la température de 600°C.
- Procédé selon la revendication 3, caractérisé en ce qu'on confère ladite vitesse de refroidissement à ladite bande par projection sur la surface de la bande d'un fluide refroidissant.
- Bande d'acier inoxydable ferritique du type contenant au plus 0,012% de carbone, au plus 1% de manganèse, au plus 1% de silicium, au plus 0,040% de phosphore, au plus 0,030% de soufre et entre 16 et 18% de chrome, caractérisée en ce qu'elle est susceptible d'être obtenue par le procédé selon l'une des revendications 1 à 5.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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FR9706576 | 1997-05-29 | ||
FR9706576A FR2763960B1 (fr) | 1997-05-29 | 1997-05-29 | Procede de fabrication de bandes minces d'acier inoxydable ferritique, et bandes minces ainsi obtenues |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0881305A1 true EP0881305A1 (fr) | 1998-12-02 |
EP0881305B1 EP0881305B1 (fr) | 2003-01-29 |
Family
ID=9507357
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98401090A Expired - Lifetime EP0881305B1 (fr) | 1997-05-29 | 1998-05-06 | Procédé de fabrication de bandes minces d'acier inoxydable ferritique |
Country Status (24)
Country | Link |
---|---|
US (1) | US6106638A (fr) |
EP (1) | EP0881305B1 (fr) |
JP (1) | JP4224733B2 (fr) |
KR (1) | KR100538683B1 (fr) |
CN (1) | CN1078113C (fr) |
AT (1) | ATE231925T1 (fr) |
AU (1) | AU706022B2 (fr) |
BR (1) | BR9801552A (fr) |
CA (1) | CA2238803C (fr) |
CZ (1) | CZ291528B6 (fr) |
DE (1) | DE69810988T2 (fr) |
DK (1) | DK0881305T3 (fr) |
ES (1) | ES2191263T3 (fr) |
FR (1) | FR2763960B1 (fr) |
ID (1) | ID20384A (fr) |
MX (1) | MXPA98004218A (fr) |
PL (1) | PL187133B1 (fr) |
RO (1) | RO120322B1 (fr) |
RU (1) | RU2192483C2 (fr) |
SK (1) | SK284091B6 (fr) |
TR (1) | TR199800976A2 (fr) |
TW (1) | TW369446B (fr) |
UA (1) | UA55398C2 (fr) |
ZA (1) | ZA984147B (fr) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2790485A1 (fr) * | 1999-03-05 | 2000-09-08 | Usinor | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
EP1099773A1 (fr) * | 1999-03-30 | 2001-05-16 | Kawasaki Steel Corporation | Plaque en acier inoxydable ferritique |
EP1118687A1 (fr) * | 2000-01-21 | 2001-07-25 | Nisshin Steel Co., Ltd. | Tôle d'acier inoxydable martensitique à résistance et tenacité éléveés, procédé d'inhibition des fissures marginales pendant le laminage à froid, et procédé pour la production du tôle d'acier |
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US6500284B1 (en) * | 1998-06-10 | 2002-12-31 | Suraltech, Inc. | Processes for continuously producing fine grained metal compositions and for semi-solid forming of shaped articles |
DE10046181C2 (de) * | 2000-09-19 | 2002-08-01 | Krupp Thyssen Nirosta Gmbh | Verfahren zum Herstellen eines überwiegend aus Mn-Austenit bestehenden Stahlbands oder -blechs |
EP1326725B1 (fr) * | 2000-09-29 | 2009-08-05 | Nucor Corporation | Production de bandes d'acier fines |
CA2378934C (fr) | 2002-03-26 | 2005-11-15 | Ipsco Inc. | Acier micro-allie a haute resistance et methode de fabrication dudit produit |
US7220325B2 (en) * | 2002-04-03 | 2007-05-22 | Ipsco Enterprises, Inc. | High-strength micro-alloy steel |
US8158057B2 (en) | 2005-06-15 | 2012-04-17 | Ati Properties, Inc. | Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells |
US7842434B2 (en) * | 2005-06-15 | 2010-11-30 | Ati Properties, Inc. | Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells |
US7981561B2 (en) * | 2005-06-15 | 2011-07-19 | Ati Properties, Inc. | Interconnects for solid oxide fuel cells and ferritic stainless steels adapted for use with solid oxide fuel cells |
JP4514032B2 (ja) * | 2004-06-10 | 2010-07-28 | 新日鐵住金ステンレス株式会社 | 塗装密着性の良好なフェライト系ステンレス鋼帯の製造方法 |
DE102005063058B3 (de) * | 2005-12-29 | 2007-05-24 | Thyssenkrupp Nirosta Gmbh | Verfahren zum Herstellen eines Kaltbands mit ferritischem Gefüge |
EP2406404B1 (fr) * | 2009-03-11 | 2017-08-23 | Salzgitter Flachstahl GmbH | Procédé de production d'un feuillard à chaud par coulée horizontale à partir d'acier ferritique |
CN101607266A (zh) * | 2009-07-20 | 2009-12-23 | 山东泰山钢铁集团有限公司 | 一种适用于炉卷轧机生产铁素体不锈钢热轧钢带的方法 |
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RU2615426C1 (ru) * | 2015-12-03 | 2017-04-04 | Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") | Способ производства горячекатаной высокопрочной коррозионно-стойкой стали |
CN107142364A (zh) * | 2017-04-27 | 2017-09-08 | 酒泉钢铁(集团)有限责任公司 | 一种超纯铁素体不锈钢双辊薄带铸轧生产工艺 |
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- 1997-05-29 FR FR9706576A patent/FR2763960B1/fr not_active Expired - Fee Related
-
1998
- 1998-05-06 DE DE69810988T patent/DE69810988T2/de not_active Expired - Lifetime
- 1998-05-06 DK DK98401090T patent/DK0881305T3/da active
- 1998-05-06 EP EP98401090A patent/EP0881305B1/fr not_active Expired - Lifetime
- 1998-05-06 AT AT98401090T patent/ATE231925T1/de active
- 1998-05-06 ES ES98401090T patent/ES2191263T3/es not_active Expired - Lifetime
- 1998-05-11 US US09/075,533 patent/US6106638A/en not_active Expired - Fee Related
- 1998-05-12 AU AU64835/98A patent/AU706022B2/en not_active Ceased
- 1998-05-12 TW TW087107288A patent/TW369446B/zh not_active IP Right Cessation
- 1998-05-18 ZA ZA984147A patent/ZA984147B/xx unknown
- 1998-05-21 SK SK678-98A patent/SK284091B6/sk not_active IP Right Cessation
- 1998-05-27 UA UA98052764A patent/UA55398C2/uk unknown
- 1998-05-27 CA CA002238803A patent/CA2238803C/fr not_active Expired - Fee Related
- 1998-05-27 MX MXPA98004218A patent/MXPA98004218A/es not_active IP Right Cessation
- 1998-05-28 RU RU98110130/02A patent/RU2192483C2/ru not_active IP Right Cessation
- 1998-05-28 KR KR1019980019509A patent/KR100538683B1/ko not_active IP Right Cessation
- 1998-05-28 RO RO98-01021A patent/RO120322B1/ro unknown
- 1998-05-28 BR BR9801552A patent/BR9801552A/pt not_active IP Right Cessation
- 1998-05-28 CN CN98102980A patent/CN1078113C/zh not_active Expired - Fee Related
- 1998-05-28 ID IDP980784A patent/ID20384A/id unknown
- 1998-05-28 CZ CZ19981658A patent/CZ291528B6/cs not_active IP Right Cessation
- 1998-05-29 TR TR1998/00976A patent/TR199800976A2/xx unknown
- 1998-05-29 JP JP14893198A patent/JP4224733B2/ja not_active Expired - Fee Related
- 1998-05-29 PL PL98326582A patent/PL187133B1/pl not_active IP Right Cessation
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Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2790485A1 (fr) * | 1999-03-05 | 2000-09-08 | Usinor | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
WO2000053817A1 (fr) * | 1999-03-05 | 2000-09-14 | Usinor | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
US6588494B1 (en) | 1999-03-05 | 2003-07-08 | Usinor | Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips |
EP1099773A1 (fr) * | 1999-03-30 | 2001-05-16 | Kawasaki Steel Corporation | Plaque en acier inoxydable ferritique |
EP1099773A4 (fr) * | 1999-03-30 | 2003-05-07 | Kawasaki Steel Co | Plaque en acier inoxydable ferritique |
USRE40950E1 (en) | 1999-03-30 | 2009-11-10 | Jfe Steel Corporation | Ferritic stainless steel plate |
EP1118687A1 (fr) * | 2000-01-21 | 2001-07-25 | Nisshin Steel Co., Ltd. | Tôle d'acier inoxydable martensitique à résistance et tenacité éléveés, procédé d'inhibition des fissures marginales pendant le laminage à froid, et procédé pour la production du tôle d'acier |
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