EP0881305B1 - Procédé de fabrication de bandes minces d'acier inoxydable ferritique - Google Patents
Procédé de fabrication de bandes minces d'acier inoxydable ferritique Download PDFInfo
- Publication number
- EP0881305B1 EP0881305B1 EP98401090A EP98401090A EP0881305B1 EP 0881305 B1 EP0881305 B1 EP 0881305B1 EP 98401090 A EP98401090 A EP 98401090A EP 98401090 A EP98401090 A EP 98401090A EP 0881305 B1 EP0881305 B1 EP 0881305B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- strip
- temperature
- carbides
- cooling
- austenite
- 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
-
- 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
-
- 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
-
- 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 particularly, it relates to the casting of ferritic stainless steels directly from liquid metal in the form of strips a few mm thick.
- the winding of the strip most often occurs at a temperature of the order of 700 to 900 ° C., depending on its thickness. and the casting speed.
- the winding temperature also depends, of course, on the distance between the rolls and the winder.
- the wound strip is then left to cool naturally, before subjecting it to metallurgical treatments comparable to those usually carried out on hot-rolled strips made from conventional continuous casting slabs.
- the fragility of the metal is precisely attributed to these large carbides, the size of which is around 1 to 5 ⁇ m. They constitute sites of initiation for the ruptures which propagate by cleavage in the surrounding ferritic matrix: their harmful effect is added to that of the columnar structure with large grains.
- Document JP-A-5293595 recommends carrying out the winding at a temperature of 700 to 200 ° C., while giving the steel low carbon and nitrogen contents (0.030% or less) and a niobium content of 0 , 1 to 1% acting as a stabilizer.
- ⁇ p 420 x% C + 470 x% N + 23 x% Ni + 9 x% Cu + 7 x% Mn - 11.5 x% Cr - 11.5 x% Si - 12 x% Mo - 23 x% V - 47 x% Nb - 49 x% Ti - 52 x% Al + 189.
- the object of the invention is to propose an economical mode of production of thin strips of ferritic stainless steel of the AISI 430 and related types by casting between cylinders, which provides said strips with sufficient ductility to allow operations of unwinding, shearing of edges and cold processing (pickling, rolling ...) to take place without incidents such as strip breakage or the appearance of cracks on the edges.
- this process should not include steps requiring the addition of complex facilities to a standard cylinder casting machine. Neither should it make it necessary to carry out an elaboration of the liquid metal aimed at obtaining very low contents of elements such as carbon and nitrogen, as well as the addition of elements of expensive alloys.
- the subject of the invention is a method of manufacturing ferritic stainless steel strips, according to which, directly from liquid metal, it is solidified between two close cylinders with horizontal axes, internally cooled and turning in direction contrary, a strip of ferritic stainless steel of the type containing at most 0.12% of carbon, at most 1% of manganese, at most 1% of silicon, at most 0.040% of phosphorus, at most 0.030% of sulfur and between 16 and 18% chromium, characterized in that the said strip is then cooled or allowed to cool while avoiding making it stay in the field of transformation of austenite into ferrite and carbides, in that the winding is carried out of said strip at a temperature between 600 ° C and the martensitic transformation temperature Ms, in that the wound strip is allowed to cool at a maximum speed of 300 ° C / h to a temperature between 200 ° C and ambient temperature, and in that a closed annealing of said strip is then carried out.
- the invention consists, starting from a strip of ferritic stainless steel of standard composition cast between cylinders, to cool and to wind said strip under special conditions, before subjecting it to annealing. closed.
- This treatment essentially aims to limit as much as possible the formation of large embrittling carbides. For this, it is necessary to limit the precipitation of carbides and to favor the transformation of austenite into martensite in the raw casting stage, while 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 allowing the strip to cool naturally in the open air after it leaves the casting rolls, and of winding it at around 800 ° C., while it is found in the precipitation zone of chromium carbides at ferritic joints and at ferrite-austenite interfaces. This winding causes, as has been said, a considerable slowing down of the cooling of the strip, which is then forced to remain for a long time in the zone for transforming austenite into ferrite and chromium carbides, before returning to ambient temperature. .
- Treatment B consists in letting the strip cool naturally in the open air, allowing it to reach room temperature without winding it.
- the strip does not remain in the zone of transformation of austenite into ferrite and chromium carbides, but it undergoes a significant martensitic transformation between the temperatures Ms and Mf. We will see why such a treatment cannot be included in the invention.
- Treatment C which is representative of the invention, consists in first allowing the strip to cool naturally, without being wound, so as to avoid it staying in the zone for transforming austenite into ferrite and chromium carbides, and winding only at a temperature of around 600 ° C. During the cooling of the wound strip, 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 approximately 300 ° C. This temperature remains however imperatively higher than Ms (which depends on the chemical composition of the steel), and during the cooling of the coil this prevents the strip from staying in the area where the martensitic transformation would take place in a very significant way. Its final thermal path joins those of treatments A and C.
- the picture in Figure 2 shows a portion of a sample of a reference strip which has followed the thermal path A in Figure 1 (therefore a winding at 800 ° C) to be brought in wound form at room temperature, then underwent closed 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. It is observed that the majority of the sample consists of large ferritic grains 3.
- the zones 4 comprising small ferritic grains resulting from the transformation of martensite ⁇ 'during closed annealing represent only a minority fraction of l 'sample. We especially notice the presence, within the structure, of continuous films of chromium carbides 5.
- FIG. 3 shows a portion of a sample of a strip according to the invention (of the same composition and thickness as that of FIG. 2) which has followed an intermediate thermal path between paths C and D in the figure 1 to room temperature (the strip was wound at 500 ° C.), then underwent closed cup annealing identical to that undergone by the reference sample of FIG. 2. It is observed that the large ferritic grains 3 are always present, but that the zones with small ferritic grains 6 resulting from the transformation of the martensite ⁇ 'are in greater proportion.
- 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 was, in this reference case, 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 strip leaving the cylinders a cooling path which makes it possible to limit the precipitation of carbides, avoiding above all those which could come from the decomposition of austenite and which are likely to coalesce into large continuous films during closed annealing.
- the second idea is to promote, at the same stage of development, the transformation of austenite into martensite so as to obtain as much as possible of fine-grained ferrite during closed annealing. These conditions are achieved if the time spent by the cast strip is limited in the area of precipitation of carbides and nitrides from ferrite, and especially if it is avoided from staying in the area of transformation of austenite into ferrite and carbides.
- the imposition on the strip of a cooling speed greater than or equal to 10 ° C / s between its exit from the cylinders and the moment when it reaches the temperature of 600 ° C from which the winding can take place generally provides the desired results.
- closed annealing should be carried out on a coil whose temperature is initially between ambient and 200 ° C. It is typically carried out 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 grade such as incorporation of stabilizers and / or lowering of carbon and nitrogen contents to unusually low levels. It can be carried out on a continuous casting machine between rolls which does not need to be equipped with a hot rolling installation of the strip leaving the rolls. It also does not require any special adaptations to the stages of the manufacturing cycle after casting (closed cup annealing, shearing of edges, pickling, etc.). The only modification to a standard roll-to-roll installation that its installation is likely to require is the possible addition of a device for cooling the strip under the rolls.
- Such a device which could be of very simple design, would make it possible to ensure that the strip never stays in the field of transformation of austenite into ferrite and carbides and that the winding is always carried out 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 on the other hand may be desirable for the casting of other types of steel).
- This composition corresponds to a ⁇ p criterion of 46.5% and to an Ac1 temperature of 826 ° C.
- a winding carried out at 500 ° C. provides the strip with energy absorbed at 20 ° C (after closed annealing) of 160 J / cm 2 , for test conditions 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)
- Chemical Vapour Deposition (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Rolling (AREA)
- Catalysts (AREA)
- Wrappers (AREA)
- Artificial Fish Reefs (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9706576A FR2763960B1 (fr) | 1997-05-29 | 1997-05-29 | Procede de fabrication de bandes minces d'acier inoxydable ferritique, et bandes minces ainsi obtenues |
FR9706576 | 1997-05-29 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0881305A1 EP0881305A1 (fr) | 1998-12-02 |
EP0881305B1 true 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 (es) |
EP (1) | EP0881305B1 (es) |
JP (1) | JP4224733B2 (es) |
KR (1) | KR100538683B1 (es) |
CN (1) | CN1078113C (es) |
AT (1) | ATE231925T1 (es) |
AU (1) | AU706022B2 (es) |
BR (1) | BR9801552A (es) |
CA (1) | CA2238803C (es) |
CZ (1) | CZ291528B6 (es) |
DE (1) | DE69810988T2 (es) |
DK (1) | DK0881305T3 (es) |
ES (1) | ES2191263T3 (es) |
FR (1) | FR2763960B1 (es) |
ID (1) | ID20384A (es) |
MX (1) | MXPA98004218A (es) |
PL (1) | PL187133B1 (es) |
RO (1) | RO120322B1 (es) |
RU (1) | RU2192483C2 (es) |
SK (1) | SK284091B6 (es) |
TR (1) | TR199800976A3 (es) |
TW (1) | TW369446B (es) |
UA (1) | UA55398C2 (es) |
ZA (1) | ZA984147B (es) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102005063058B3 (de) * | 2005-12-29 | 2007-05-24 | Thyssenkrupp Nirosta Gmbh | Verfahren zum Herstellen eines Kaltbands mit ferritischem Gefüge |
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 |
Families Citing this family (19)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
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 |
FR2790485B1 (fr) | 1999-03-05 | 2002-02-08 | Usinor | Procede de coulee continue entre cylindres de bandes d'acier inoxydable ferritique a haute ductilite, et bandes minces ainsi obtenues |
DE60025703T2 (de) | 1999-03-30 | 2006-08-31 | Jfe Steel Corp. | Ferritische rostfreie stahlplatte |
JP4518645B2 (ja) * | 2000-01-21 | 2010-08-04 | 日新製鋼株式会社 | 高強度高靱性マルテンサイト系ステンレス鋼板並びに冷延耳切れ抑止方法および鋼板製造法 |
DE10046181C2 (de) * | 2000-09-19 | 2002-08-01 | Krupp Thyssen Nirosta Gmbh | Verfahren zum Herstellen eines überwiegend aus Mn-Austenit bestehenden Stahlbands oder -blechs |
AU9150501A (en) * | 2000-09-29 | 2002-04-08 | Ishikawajima Harima Heavy Ind | Production of thin steel strip |
CA2378934C (en) | 2002-03-26 | 2005-11-15 | Ipsco Inc. | High-strength micro-alloy steel and process for making same |
US7220325B2 (en) * | 2002-04-03 | 2007-05-22 | Ipsco Enterprises, Inc. | High-strength micro-alloy steel |
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 |
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 |
KR101563606B1 (ko) * | 2009-03-11 | 2015-10-27 | 잘쯔기터 플래시슈탈 게엠베하 | 열간압연 스트립을 제조하는 방법 및 페라이트계 강으로부터 제조된 열간압연 스트립 |
KR101312776B1 (ko) * | 2009-12-21 | 2013-09-27 | 주식회사 포스코 | 마르텐사이트계 스테인리스강 및 그 제조방법 |
CN102211179B (zh) * | 2010-04-09 | 2013-01-02 | 中国科学院金属研究所 | 一种应用于大型马氏体不锈钢铸件的高温打箱工艺 |
KR101614614B1 (ko) * | 2014-10-22 | 2016-04-22 | 주식회사 포스코 | 고강도, 고연성의 페라이트계 스테인리스 강판 및 그의 제조방법 |
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 |
CN114959466B (zh) * | 2022-05-17 | 2023-06-13 | 天津太钢天管不锈钢有限公司 | 一种低铬铁素体不锈钢及其制造方法 |
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JPS57155326A (en) * | 1981-03-23 | 1982-09-25 | Nippon Steel Corp | Production of ferritic stainless steel sheet excellent in workability |
ES2021211A6 (es) * | 1990-03-01 | 1991-10-16 | Acerinox Sa | Procedimiento mejorado de laminacion en caliente en un tren steckel. |
FR2665652A1 (fr) * | 1990-08-13 | 1992-02-14 | Usinor Sacilor | Procede et dispositif de fabrication d'une bande en acier inoxydable semi-ferritique a partir de metal en fusion. |
JP3141120B2 (ja) * | 1992-02-21 | 2001-03-05 | 株式会社トプコン | 位相測定装置及び距離測定装置 |
JP3001718B2 (ja) * | 1992-04-17 | 2000-01-24 | 新日本製鐵株式会社 | フェライト系ステンレス鋼薄肉鋳片の製造方法 |
JP2682335B2 (ja) * | 1992-06-01 | 1997-11-26 | 住友金属工業株式会社 | フェライト系ステンレス鋼熱延鋼帯の製造法 |
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 |
CN1044388C (zh) * | 1994-01-26 | 1999-07-28 | 川崎制铁株式会社 | 耐腐蚀性极好的不锈钢板的生产方法 |
JPH08295943A (ja) * | 1995-04-27 | 1996-11-12 | Nippon Steel Corp | 冷延表面性状の優れたフェライト系ステンレス鋼薄板の製造方法 |
JP3879164B2 (ja) * | 1997-03-18 | 2007-02-07 | Jfeスチール株式会社 | 冷間圧延性に優れたフェライト系ステンレス熱延鋼帯の製造方法 |
-
1997
- 1997-05-29 FR FR9706576A patent/FR2763960B1/fr not_active Expired - Fee Related
-
1998
- 1998-05-06 ES ES98401090T patent/ES2191263T3/es not_active Expired - Lifetime
- 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
- 1998-05-11 US US09/075,533 patent/US6106638A/en not_active Expired - Fee Related
- 1998-05-12 TW TW087107288A patent/TW369446B/zh not_active IP Right Cessation
- 1998-05-12 AU AU64835/98A patent/AU706022B2/en not_active Ceased
- 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 CN CN98102980A patent/CN1078113C/zh not_active Expired - Fee Related
- 1998-05-28 RO RO98-01021A patent/RO120322B1/ro unknown
- 1998-05-28 ID IDP980784A patent/ID20384A/id unknown
- 1998-05-28 KR KR1019980019509A patent/KR100538683B1/ko not_active IP Right Cessation
- 1998-05-28 CZ CZ19981658A patent/CZ291528B6/cs not_active IP Right Cessation
- 1998-05-28 BR BR9801552A patent/BR9801552A/pt not_active IP Right Cessation
- 1998-05-28 RU RU98110130/02A patent/RU2192483C2/ru not_active IP Right Cessation
- 1998-05-29 TR TR1998/00976A patent/TR199800976A3/tr 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
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE102005063058B3 (de) * | 2005-12-29 | 2007-05-24 | Thyssenkrupp Nirosta Gmbh | Verfahren zum Herstellen eines Kaltbands mit ferritischem Gefüge |
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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