EP1163376B1 - Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues - Google Patents
Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues Download PDFInfo
- Publication number
- EP1163376B1 EP1163376B1 EP00909393A EP00909393A EP1163376B1 EP 1163376 B1 EP1163376 B1 EP 1163376B1 EP 00909393 A EP00909393 A EP 00909393A EP 00909393 A EP00909393 A EP 00909393A EP 1163376 B1 EP1163376 B1 EP 1163376B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- stainless steel
- ferritic stainless
- less
- casting
- strips
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
Classifications
-
- 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
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
-
- 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
- C21D8/021—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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
- C21D8/0415—Rapid solidification; Thin strip casting
Definitions
- the invention relates to the continuous casting of metals, and more precisely the casting continuous, directly from liquid metal, of stainless steel strips of the type ferritic whose thickness is of the order of a few mm, by the process known as "casting between cylinders ".
- the process mainly used today is pouring of said liquid metal between two internally cooled cylinders, rotating around their horizontal axes in opposite directions, and arranged parallel to each other, the minimum distance between their surfaces being substantially equal to the thickness that is desired impart to the cast strip (for example a few mm).
- the casting space containing liquid steel is defined by the lateral surfaces of the cylinders, on which the solidification of the strip, and by side closing plates in refractory applied against the ends of the cylinders.
- the liquid metal initiates its solidification on contact with external surfaces of the cylinders, on which it forms solidified "skins", of which ensures that they meet at the "neck", that is to say the area where the distance between cylinders is minimum.
- Thin strips of ferritic stainless steel obtained by continuous casting between two cylinders have a significant brittleness, which makes their cold processing during normal operations such as unwinding, shearing edges or cold rolling.
- the high hardness of these ferritic grains supersaturated with interstitial elements such as carbon and nitrogen is an aggravating factor for the fragility of thin strips.
- document EP-A-0 881 305 describes an unstabilized ferritic grade, which is obtained by direct casting of a strip between cylinders, the strip then being wound at a temperature below 600 ° C. It is then annealed in a vacuum, always in coiled form. Winding below 600 ° C limits precipitation carbides in the raw casting stage, and thus avoid their coalescence in the form of films very weakening continuous during closed annealing.
- Document EP-A-0 638 653 recommends the casting of a ferritic grade with a chromium content which can be relatively high (13-25%) stabilized with titanium, niobium or aluminum (0.05% at least), low carbon and nitrogen contents, and having a negative ⁇ p index, ⁇ p being the maximum amount of austenite formed at high temperature.
- hot rolling is carried out with a reduction rate greater than 5% in the range 950-1150 ° C, followed by slow cooling to less than 20 ° C / s or a high temperature hold for more than 5 seconds.
- the winding of the strip then takes place at less than 700 ° C.
- the cold winding prevents the formation of fragile intermetallic phases.
- Document JP - A - 08283845 recommends an asynchronous hot rolling of a strip cast at an initial thickness of less than 10 mm, having the effect of improving the ductility by refining the structure of the thin strips by recrystallization. The flow is followed by asynchronous hot rolling and heat treatment. We are trying to improve here the ductility of the thin strips by a recrystallization treatment.
- a band is cast between cylinders whose index ⁇ 'p is greater than 25%, it is hot rolled with a reduction rate greater than 20% at less than 1200 ° C, then it is puts in coils and performs a closed annealing of the coils between 700 and 900 ° C for 4 hours.
- the aim is to obtain a strip with excellent surface quality, without we are particularly interested in its ductility.
- the object of the invention is to provide steelmakers with a manufacturing process, by casting between cylinders, thin strips of ferritic stainless steel to be subjected thereafter conventional cold processing, without requiring complex or costly operations such as controlled strip cooling or closed annealing to provide said strips have good ductility.
- the subject of the invention is also thin strips capable of being obtained by the previous process.
- the invention consists in associating the presence of one or several stabilizing elements in significant quantities at levels of other elements alloy which nevertheless maintain the index ⁇ p at a high value, and at a winding of the strip at a relatively low temperature.
- the conjunction of stabilizing elements and a high ⁇ p index was not known in the prior art, a fortiori its association with a low winding temperature which allows these analytical characteristics to be reconciled with very good ductility of the strip, without, moreover, that it is necessary to proceed with controlled cooling of the strip or a time-consuming heat treatment and in energy.
- Chromium content above 11% meets usual requirements encountered in ferritic stainless steels. The maximum of 18% is justified in this that beyond this limit, the ductile-brittle transition temperature of steels stainless steel increases significantly, and the invention then becomes ineffective. Chromium has also tend to significantly decrease the value of the ⁇ p index.
- the silicon and molybdenum contents are maintained respectively at 1% and 2.5% maximum, to avoid the formation of intermetallic compounds or the formation ⁇ or ⁇ type intermetallic phases.
- the maximum silicon content is also more or less consistent with those encountered on conventional ferritic grades, such as the maximum manganese content of 1%.
- the total content of stabilizing elements namely titanium, niobium, zirconium and aluminum, must be greater than or equal to 0.05% so that they can play their role usual. Above 1%, problems of flowability of the liquid steel are observed. through the nozzles of the casting installation, as well as the presence of surface defects on the strip which can constitute the beginnings of ruptures. We must also ensure that that a significant presence of stabilizing elements does not lower the ⁇ p index to a value which would be excessively low, if otherwise silicon, molybdenum and vanadium are present at high contents. At the same time, the total carbon content and nitrogen should not exceed 0.05% to avoid forming an excessive amount of carbides or of embrittling carbonitrides.
- the ⁇ p index is less than 30%, the high-ferrite-austenite two-phase temperature, after the end of solidification, is not sufficient to allow a refinement of the strip structure and significantly improve the ductility of the product sank. If the index ⁇ p is greater than 60%, the ductility deteriorates, because the contraction resulting from the transformation of ferrite-austenite phase at high temperature risk of lead to the appearance of surface defects such as cracks, which constitute as much possible initiations of ruptures during subsequent processing operations.
- the grades A, B and C are essentially distinguished in that the grade A is stabilized with titanium, grade B is stabilized with niobium and grade C is stabilized by these two elements at the same time. In this last nuance, the simultaneous presence of fairly high contents of these two stabilizers, as well as the higher silicon content higher than in grades A and B, resulted in a lowering of the ⁇ p index below of the 30% limit required by the invention.
- Table 2 groups together the particular test conditions to which the preceding steels were subjected, in terms of reduction rate and temperature during possible hot rolling, and in terms of winding temperature. The results of the impact bending tests on Charpy specimens to which the strips were subjected after their winding were also reported therein, with the aim of determining their breaking energy at a temperature of 0 ° C. For this purpose, V-notched test pieces were used. It is considered that a breaking energy of less than 40 J / cm 2 is insufficient to provide the strips with properties guaranteeing unwinding without incident and to allow the usual cold transformations.
- Hot rolling temperature (° C) Winding temperature (° C) Breaking energy at 0 ° C (J / cm 2 ) 1 (reference) AT - - 800 35 2 (invention) AT - - 500 85 3 (reference) B - - 800 20 4 (reference) VS - - 500 30 5 (reference) AT 10 1000 800 34 6 (invention) AT 10 1000 500 185
- Tests 1 to 3 were carried out on steels whose ⁇ p index was greater than 30%, in accordance with the invention. They illustrate the beneficial effect of a low temperature winding on the ductility of the strip, in that only test 2 where the winding took place at 500 ° C. gave rise to satisfactory ductility of the cast strip, because we managed to avoid the formation of embrittling precipitates in the coiled steel. This is not possible when the winding is carried out at 800 ° C (tests 1 and 3), and the breaking energy by Charpy test is then below the lower limit of 40 J / cm 2 that we consider satisfactory.
- test 4 the winding was indeed carried out at a temperature of 500 ° C., in accordance with the invention, and the formation of embrittling precipitates was not observed.
- this test related to a shade whose ⁇ p index was less than the 30% required by the invention, and the amount of hot formed austenite was insufficient to allow a very substantial refinement of the coarse-grained structure obtained after solidification. Consequently, and despite the presence in high quantity of stabilizing elements, the The ductility of the strip after winding was no more satisfactory than after tests 1 and 3.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Catalysts (AREA)
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9902749 | 1999-03-05 | ||
FR9902749A FR2790485B1 (fr) | 1999-03-05 | 1999-03-05 | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
PCT/FR2000/000498 WO2000053817A1 (fr) | 1999-03-05 | 2000-02-29 | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1163376A1 EP1163376A1 (fr) | 2001-12-19 |
EP1163376B1 true EP1163376B1 (fr) | 2002-12-04 |
Family
ID=9542860
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP00909393A Expired - Lifetime EP1163376B1 (fr) | 1999-03-05 | 2000-02-29 | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
Country Status (14)
Country | Link |
---|---|
US (1) | US6588494B1 (ko) |
EP (1) | EP1163376B1 (ko) |
JP (1) | JP4499923B2 (ko) |
KR (1) | KR100637790B1 (ko) |
AT (1) | ATE229086T1 (ko) |
AU (1) | AU757018B2 (ko) |
BR (1) | BR0008700A (ko) |
DE (1) | DE60000924T2 (ko) |
DK (1) | DK1163376T3 (ko) |
ES (1) | ES2185574T3 (ko) |
FR (1) | FR2790485B1 (ko) |
PT (1) | PT1163376E (ko) |
TW (1) | TW503138B (ko) |
WO (1) | WO2000053817A1 (ko) |
Families Citing this family (23)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1326725B1 (en) * | 2000-09-29 | 2009-08-05 | Nucor Corporation | Production of thin steel strip |
US7117925B2 (en) * | 2000-09-29 | 2006-10-10 | Nucor Corporation | Production of thin steel strip |
US7485196B2 (en) * | 2001-09-14 | 2009-02-03 | Nucor Corporation | Steel product with a high austenite grain coarsening temperature |
ITRM20010584A1 (it) * | 2001-09-26 | 2003-03-26 | Acciai Speciali Terni Spa | Acciaio inossidabile ferritico e suo uso nella fabbricazione di manufatti per impieghi ad elevate temperature. |
WO2003057100A2 (en) | 2002-01-10 | 2003-07-17 | Katana Technologies Gmbh | Device and procedure for refractive laser surgery |
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 |
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 |
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 |
DE10339595A1 (de) * | 2003-08-26 | 2005-04-07 | Siemens Ag | Verfahren zur Vorhersage und Steuerung der Vergießbarkeit von Flüssigstahl |
US7484551B2 (en) * | 2003-10-10 | 2009-02-03 | Nucor Corporation | Casting steel strip |
TR201902554T4 (tr) * | 2003-10-10 | 2019-03-21 | Nucor Corp | Çelik şerit döküm. |
JP4959937B2 (ja) * | 2004-12-27 | 2012-06-27 | 株式会社日立産機システム | 腐食診断部品を設けてなる配電用変圧器 |
US9149868B2 (en) * | 2005-10-20 | 2015-10-06 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
US9999918B2 (en) | 2005-10-20 | 2018-06-19 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
US10071416B2 (en) * | 2005-10-20 | 2018-09-11 | Nucor Corporation | High strength thin cast strip product and method for making the same |
US20070267110A1 (en) * | 2006-05-17 | 2007-11-22 | Ipsco Enterprises, Inc. | Method for making high-strength steel pipe, and pipe made by that method |
US7975754B2 (en) * | 2007-08-13 | 2011-07-12 | Nucor Corporation | Thin cast steel strip with reduced microcracking |
US20110277886A1 (en) | 2010-02-20 | 2011-11-17 | Nucor Corporation | Nitriding of niobium steel and product made thereby |
RU2452788C2 (ru) * | 2010-02-27 | 2012-06-10 | Российская Федерация, от имени которой выступает Министерство образования и науки РФ (Минобрнаука РФ) | Наноструктурированная ферритная коррозионно-стойкая сталь |
CN102303212B (zh) * | 2011-06-24 | 2013-04-10 | 成都申信达机械有限公司 | 一种湿喷机衬板的制造工艺 |
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 |
CN109731913B (zh) * | 2019-02-21 | 2020-07-24 | 江苏沙钢集团有限公司 | 一种降低双辊连铸产线轧机轧制力的方法 |
WO2024128560A1 (ko) * | 2022-12-12 | 2024-06-20 | 주식회사 포스코 | 성형성이 향상된 페라이트계 스테인리스강 및 그 제조방법 |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0247264B1 (en) * | 1986-05-24 | 1992-07-22 | Nippon Steel Corporation | Method for producing a thin casting of cr-series stainless steel |
JPH06220545A (ja) * | 1993-01-28 | 1994-08-09 | Nippon Steel Corp | 靱性の優れたCr系ステンレス鋼薄帯の製造方法 |
JP3314834B2 (ja) * | 1993-10-19 | 2002-08-19 | 新日本製鐵株式会社 | リビング性に優れたフェライト系ステンレス鋼板の製造方法 |
JP3779784B2 (ja) * | 1996-12-17 | 2006-05-31 | 新日本製鐵株式会社 | 表面特性に優れたフェライト系ステンレス鋼の製造方法 |
FR2763960B1 (fr) * | 1997-05-29 | 1999-07-16 | Usinor | Procede de fabrication de bandes minces d'acier inoxydable ferritique, et bandes minces ainsi obtenues |
-
1999
- 1999-03-05 FR FR9902749A patent/FR2790485B1/fr not_active Expired - Fee Related
-
2000
- 2000-02-29 DE DE60000924T patent/DE60000924T2/de not_active Expired - Lifetime
- 2000-02-29 WO PCT/FR2000/000498 patent/WO2000053817A1/fr active IP Right Grant
- 2000-02-29 DK DK00909393T patent/DK1163376T3/da active
- 2000-02-29 PT PT00909393T patent/PT1163376E/pt unknown
- 2000-02-29 BR BR0008700-9A patent/BR0008700A/pt not_active IP Right Cessation
- 2000-02-29 JP JP2000603438A patent/JP4499923B2/ja not_active Expired - Fee Related
- 2000-02-29 KR KR1020017011272A patent/KR100637790B1/ko active IP Right Grant
- 2000-02-29 US US09/914,430 patent/US6588494B1/en not_active Expired - Lifetime
- 2000-02-29 ES ES00909393T patent/ES2185574T3/es not_active Expired - Lifetime
- 2000-02-29 AT AT00909393T patent/ATE229086T1/de active
- 2000-02-29 EP EP00909393A patent/EP1163376B1/fr not_active Expired - Lifetime
- 2000-02-29 AU AU31696/00A patent/AU757018B2/en not_active Ceased
- 2000-03-04 TW TW089103869A patent/TW503138B/zh not_active IP Right Cessation
Also Published As
Publication number | Publication date |
---|---|
ES2185574T3 (es) | 2003-05-01 |
EP1163376A1 (fr) | 2001-12-19 |
DE60000924T2 (de) | 2003-08-14 |
DK1163376T3 (da) | 2003-03-24 |
TW503138B (en) | 2002-09-21 |
PT1163376E (pt) | 2003-02-28 |
FR2790485B1 (fr) | 2002-02-08 |
JP4499923B2 (ja) | 2010-07-14 |
US6588494B1 (en) | 2003-07-08 |
AU3169600A (en) | 2000-09-28 |
KR100637790B1 (ko) | 2006-10-23 |
FR2790485A1 (fr) | 2000-09-08 |
KR20010102499A (ko) | 2001-11-15 |
ATE229086T1 (de) | 2002-12-15 |
DE60000924D1 (de) | 2003-01-16 |
WO2000053817A1 (fr) | 2000-09-14 |
JP2002538007A (ja) | 2002-11-12 |
BR0008700A (pt) | 2001-12-26 |
AU757018B2 (en) | 2003-01-30 |
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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 |
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17P | Request for examination filed |
Effective date: 20010808 |
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