EP1163376A1 - Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips - Google Patents
Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin stripsInfo
- Publication number
- EP1163376A1 EP1163376A1 EP00909393A EP00909393A EP1163376A1 EP 1163376 A1 EP1163376 A1 EP 1163376A1 EP 00909393 A EP00909393 A EP 00909393A EP 00909393 A EP00909393 A EP 00909393A EP 1163376 A1 EP1163376 A1 EP 1163376A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- stainless steel
- ferritic stainless
- less
- contents
- 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.)
- Granted
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 continuous casting, directly from liquid metal, of strips of stainless steel of ferritic type whose thickness is of the order of a few mm, by the so-called process. of "casting between cylinders".
- the method mainly used today is the casting 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 which it is desired to impart to the cast strip (for example a few mm).
- the pouring space containing the liquid steel is defined by the lateral surfaces of the cylinders, on which the solidification of the strip is initiated, and by refractory side closure plates applied against the ends of the cylinders.
- the liquid metal initiates its solidification on contact with the outer surfaces of the cylinders, on which it forms solidified "skins", which are made to meet at the "neck", that is to say the area where the distance between the cylinders is minimal.
- the thin ferritic stainless steel strips obtained by continuous casting between two rolls have a significant brittleness, which makes it difficult to transform them cold during usual operations such as unwinding, shearing the edges or cold rolling.
- the poor ductility of the strips cast between rolls is explained essentially by the very large grain structure resulting from the rapid solidification mode between the casting rolls, associated with a long residence time at high temperature after the solidified strip has left the grip. cylinders.
- the high hardness of these ferritic grains supersaturated with interstitial elements such as carbon and nitrogen constitutes an aggravating factor for the brittleness of the thin bands.
- the 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 a coiled form. Coiling below 600 ° C makes it possible to limit the precipitation of carbides in the raw casting stage, and thus to avoid their coalescence in the form of continuous very embrittling films during closed annealing.
- 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.
- This quantity is defined by the relation of Tricot and Lauda 420 C% + 470 N% + 23 Ni% + 9 Cu% + 7 Mn% - 11,5 Cr% -11,5 Si % - 12 Mo% - 23 V% - 47 Nb% - 49 Ti% - 52 Al% + 189
- hot rolling is carried out with a reduction rate greater than 5% in the interval 950-1 150 ° C, followed by slow cooling to less than 20 ° C / s or holding at high temperature for more than 5 seconds. The winding of the strip then takes place at less than 700 ° C.
- the aim is to avoid the formation of austenite at high temperature by imposing a negative ⁇ p index to prevent the formation of martensite on the strip, which would make it fragile.
- the presence of stabilizers leads, by the rapid solidification, to fine embrittling precipitates. Hot rolling with high temperature maintenance and slow cooling favor the precipitation, and especially the coalescence of these precipitates, which thus become harmless.
- the cold winding prevents the formation of fragile intermetallic phases.
- Document JP-A-08283845 recommends an asynchronous hot rolling of a cast strip with 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 casting is followed by an asynchronous hot rolling and a heat treatment.
- the aim here is to improve the ductility of the thin strips by a recrystallization treatment.
- a strip 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 put into coils and 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 paying particular attention to its ductility,
- the object of the invention is to provide steelmakers with a method of manufacturing, by casting between cylinders, thin strips of ferritic stainless steel which then have to undergo conventional cold processing, without requiring complex or costly operations such as controlled cooling of the strip or closed cup annealing to give said strips good ductility.
- the invention relates to a process for casting thin strips of thickness less than 10 mm in ferritic stainless steel directly from liquid metal between two cylinders cooled in rotation with parallel horizontal axes, characterized in that than :
- ferritic stainless steel contains (in percentages by weight) from 11 to 18% of chromium, less than 1% of manganese, less than 1% of silicon, less than 2.5% of molybdenum; - Said ferritic stainless steel has carbon and nitrogen contents the sum of the contents of which does not exceed 0.05%;
- Said ferritic stainless steel contains at least one of the stabilizing elements titanium, niobium, zirconium, aluminum, and the sum of their contents is between 0.05 and 1%; - the other elements present are iron and usual impurities resulting from production;
- the invention also relates to thin strips capable of being obtained by the above method.
- the invention consists in associating the presence of one or more stabilizing elements in significant quantities with contents of other alloying elements which nevertheless maintain the index ⁇ p at a high value, and with 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 makes it possible to reconcile these analytical characteristics with a very good ductility of the strip, without, moreover, that it is necessary to carry out a controlled cooling of the strip or a heat treatment penalizing in time and energy.
- the different features are motivated by the following considerations.
- the chromium content greater than 11% complies with the usual requirements encountered in ferritic stainless steels. The maximum of 18% is justified in that beyond this limit, the ductile-brittle transition temperature of stainless steels increases significantly, and the invention then becomes inoperative. Chromium also tends to strongly decrease the value of the ⁇ p index.
- the silicon and molybdenum contents are respectively maintained at 1% and 2.5% maximum, in order to avoid the formation of intermetallic compounds or the formation of intermetallic phases of type ⁇ or ⁇ .
- the maximum silicon content is moreover neither more nor less in line 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 usual role. 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 initiation of ruptures. It must also be ensured that a significant presence of stabilizing elements does not lower the ⁇ p index to a value which would be excessively low, if, moreover, silicon, molybdenum and vanadium are present at high contents. . At the same time, the total carbon and nitrogen content must not exceed 0.05% so as not to form an excessive amount of embrittling carbides or carbonitrides.
- the index ⁇ p is less than 30%, the two-phase ferrite-austenite at high temperature, after the end of solidification, is not sufficient to allow a refinement of the strip structure and to significantly improve the ductility of the cast product . If the index ⁇ p is greater than 60%, the ductility deteriorates, because the contraction resulting from the transformation of the ferrite-austenite phase at high temperature risks leading to the appearance of surface defects such as cracks, which constitute as much possible initiations of ruptures during subsequent processing operations.
- Table 1 Chemical composition of the steels studied The grades A, B and C are essentially distinguished in that the grade A is stabilized with titanium, the grade B is stabilized with niobium and the grade C is stabilized by these two elements at the same time. In this last grade, the simultaneous presence at fairly high levels of these two stabilizers, as well as the higher silicon content than in grades A and B, led to a lowering of the ⁇ p index below the limit of 30 % required by the invention.
- Table 2 groups together the specific 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 test pieces 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. To this end, 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.
- Table 2 Strip processing conditions and results of impact bending tests carried out on Charpy specimens Tests 1 to 3 were carried out on steels whose ⁇ p index was greater than
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Continuous Casting (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
- Catalysts (AREA)
Abstract
Description
Claims
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9902749 | 1999-03-05 | ||
FR9902749A FR2790485B1 (en) | 1999-03-05 | 1999-03-05 | CONTINUOUS CASTING PROCESS BETWEEN CYLINDERS OF HIGH-DUCTILITY FERRITIC STAINLESS STEEL STRIPS, AND THIN STRIPS THUS OBTAINED |
PCT/FR2000/000498 WO2000053817A1 (en) | 1999-03-05 | 2000-02-29 | Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1163376A1 true EP1163376A1 (en) | 2001-12-19 |
EP1163376B1 EP1163376B1 (en) | 2002-12-04 |
Family
ID=9542860
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP00909393A Expired - Lifetime EP1163376B1 (en) | 1999-03-05 | 2000-02-29 | Method for continuous casting of highly ductile ferritic stainless steel strips between rolls, and resulting thin strips |
Country Status (14)
Country | Link |
---|---|
US (1) | US6588494B1 (en) |
EP (1) | EP1163376B1 (en) |
JP (1) | JP4499923B2 (en) |
KR (1) | KR100637790B1 (en) |
AT (1) | ATE229086T1 (en) |
AU (1) | AU757018B2 (en) |
BR (1) | BR0008700A (en) |
DE (1) | DE60000924T2 (en) |
DK (1) | DK1163376T3 (en) |
ES (1) | ES2185574T3 (en) |
FR (1) | FR2790485B1 (en) |
PT (1) | PT1163376E (en) |
TW (1) | TW503138B (en) |
WO (1) | WO2000053817A1 (en) |
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 (en) * | 2001-09-26 | 2003-03-26 | Acciai Speciali Terni Spa | FERRITIC STAINLESS STEEL AND ITS USE IN THE MANUFACTURE OF ITEMS FOR USE AT HIGH TEMPERATURES. |
US7721743B2 (en) | 2002-01-10 | 2010-05-25 | Katana Technologies Gmbh | Device and procedure for refractive laser surgery |
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 |
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 |
DE10339595A1 (en) * | 2003-08-26 | 2005-04-07 | Siemens Ag | Method for predicting and controlling the pourability of liquid steel |
US7484551B2 (en) * | 2003-10-10 | 2009-02-03 | Nucor Corporation | Casting steel strip |
CN100574935C (en) * | 2003-10-10 | 2009-12-30 | 纽科尔公司 | The method of steel band and cast steel strip |
JP4959937B2 (en) * | 2004-12-27 | 2012-06-27 | 株式会社日立産機システム | Distribution transformer with corrosion diagnostic components |
US10071416B2 (en) * | 2005-10-20 | 2018-09-11 | Nucor Corporation | High strength thin cast strip product 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 |
US9149868B2 (en) * | 2005-10-20 | 2015-10-06 | Nucor Corporation | Thin cast strip product with microalloy additions, 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 (en) * | 2010-02-27 | 2012-06-10 | Российская Федерация, от имени которой выступает Министерство образования и науки РФ (Минобрнаука РФ) | Rustproof nanostructured ferrite steel |
CN102303212B (en) * | 2011-06-24 | 2013-04-10 | 成都申信达机械有限公司 | Process for manufacturing lining board of wet-spraying machine |
CN107142364A (en) * | 2017-04-27 | 2017-09-08 | 酒泉钢铁(集团)有限责任公司 | A kind of super-purity ferrite stainless steel double roll strip casting rolling production process |
CN109731913B (en) * | 2019-02-21 | 2020-07-24 | 江苏沙钢集团有限公司 | Method for reducing rolling force of rolling mill of double-roller continuous casting production line |
KR20240087432A (en) * | 2022-12-12 | 2024-06-19 | 주식회사 포스코 | Ferritic stainless steel with improved formability and manufacturing method therefor |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3686155T2 (en) * | 1986-05-24 | 1993-02-18 | Nippon Steel Corp | METHOD FOR PRODUCING A THIN CASTING PIECE MADE OF STAINLESS STEEL CR STEEL. |
JPH06220545A (en) * | 1993-01-28 | 1994-08-09 | Nippon Steel Corp | Production of cr-series stainless steel thin strip excellent in toughness |
JP3314834B2 (en) * | 1993-10-19 | 2002-08-19 | 新日本製鐵株式会社 | Method for producing ferritic stainless steel sheet with excellent living properties |
JP3779784B2 (en) * | 1996-12-17 | 2006-05-31 | 新日本製鐵株式会社 | Method for producing ferritic stainless steel with excellent surface properties |
FR2763960B1 (en) * | 1997-05-29 | 1999-07-16 | Usinor | PROCESS FOR PRODUCING FERRITIC STAINLESS STEEL THIN STRIPS AND THIN STRIPS THUS OBTAINED |
-
1999
- 1999-03-05 FR FR9902749A patent/FR2790485B1/en not_active Expired - Fee Related
-
2000
- 2000-02-29 EP EP00909393A patent/EP1163376B1/en not_active Expired - Lifetime
- 2000-02-29 AU AU31696/00A patent/AU757018B2/en not_active Ceased
- 2000-02-29 KR KR1020017011272A patent/KR100637790B1/en active IP Right Grant
- 2000-02-29 PT PT00909393T patent/PT1163376E/en unknown
- 2000-02-29 ES ES00909393T patent/ES2185574T3/en not_active Expired - Lifetime
- 2000-02-29 BR BR0008700-9A patent/BR0008700A/en not_active IP Right Cessation
- 2000-02-29 US US09/914,430 patent/US6588494B1/en not_active Expired - Lifetime
- 2000-02-29 WO PCT/FR2000/000498 patent/WO2000053817A1/en active IP Right Grant
- 2000-02-29 DK DK00909393T patent/DK1163376T3/en active
- 2000-02-29 JP JP2000603438A patent/JP4499923B2/en not_active Expired - Fee Related
- 2000-02-29 DE DE60000924T patent/DE60000924T2/en not_active Expired - Lifetime
- 2000-02-29 AT AT00909393T patent/ATE229086T1/en active
- 2000-03-04 TW TW089103869A patent/TW503138B/en not_active IP Right Cessation
Non-Patent Citations (1)
Title |
---|
See references of WO0053817A1 * |
Also Published As
Publication number | Publication date |
---|---|
EP1163376B1 (en) | 2002-12-04 |
JP4499923B2 (en) | 2010-07-14 |
AU3169600A (en) | 2000-09-28 |
FR2790485A1 (en) | 2000-09-08 |
US6588494B1 (en) | 2003-07-08 |
WO2000053817A1 (en) | 2000-09-14 |
DK1163376T3 (en) | 2003-03-24 |
ES2185574T3 (en) | 2003-05-01 |
FR2790485B1 (en) | 2002-02-08 |
BR0008700A (en) | 2001-12-26 |
DE60000924T2 (en) | 2003-08-14 |
DE60000924D1 (en) | 2003-01-16 |
AU757018B2 (en) | 2003-01-30 |
JP2002538007A (en) | 2002-11-12 |
ATE229086T1 (en) | 2002-12-15 |
KR20010102499A (en) | 2001-11-15 |
KR100637790B1 (en) | 2006-10-23 |
PT1163376E (en) | 2003-02-28 |
TW503138B (en) | 2002-09-21 |
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