EP0216044B1 - Process for manufacturing non-aging steel strip having a high cold formability - Google Patents

Process for manufacturing non-aging steel strip having a high cold formability Download PDF

Info

Publication number
EP0216044B1
EP0216044B1 EP86109521A EP86109521A EP0216044B1 EP 0216044 B1 EP0216044 B1 EP 0216044B1 EP 86109521 A EP86109521 A EP 86109521A EP 86109521 A EP86109521 A EP 86109521A EP 0216044 B1 EP0216044 B1 EP 0216044B1
Authority
EP
European Patent Office
Prior art keywords
max
steel
rolling
cold
maximum
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP86109521A
Other languages
German (de)
French (fr)
Other versions
EP0216044A2 (en
EP0216044B2 (en
EP0216044A3 (en
Inventor
Ernst Jürgen dr. Drewes
Bernhard Dr. Engl
Klaus Dieter Horn
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Krupp Hoesch Stahl AG
Original Assignee
Krupp Hoesch Stahl AG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=6278246&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP0216044(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Krupp Hoesch Stahl AG filed Critical Krupp Hoesch Stahl AG
Priority to AT86109521T priority Critical patent/ATE104362T1/en
Publication of EP0216044A2 publication Critical patent/EP0216044A2/en
Publication of EP0216044A3 publication Critical patent/EP0216044A3/en
Application granted granted Critical
Publication of EP0216044B1 publication Critical patent/EP0216044B1/en
Publication of EP0216044B2 publication Critical patent/EP0216044B2/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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
    • C21D8/04—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
    • C21D8/0421—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 characterised by the working steps
    • C21D8/0426—Hot rolling
    • 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
    • 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

Definitions

  • the invention relates to a method for producing an aging-resistant steel strip with high cold formability.
  • Cold rolled steel strip is widely used for the production of cold formed products.
  • different properties characteristics (characteristic values) are required, whereby in all cases of high deformation, low yield strengths and high elongation at break values are advantageous.
  • a high strengthening exponent n m is also sought for stretch-drawing processes and for deep-drawing stress, especially when producing complicated parts, for. B. of automobile bodies, the value of the vertical anisotropy r m should also be as high as possible.
  • EP-A-108 268 describes a process for the production of cold-rolled strip with the highest deep-drawability, which contains the use of low slab preheating temperatures below 1170 ° C. as a measure, but the subject of this document is IF steel with the lowest C - held by max. 0.007% C and the need to add Ti and niobium is limited.
  • the favorable effect of the low preheating temperatures is linked to the presence of (Ti.Nb) C.
  • DE-OS 31 38 302 describes a process for producing cold-rolled high-strength steel strip from a steel which has a high phosphorus content of 0.05 to 0.10% by weight. It is proposed that the steel slabs be heated to a maximum of 1,200 ° C or in the range 1,200 to 1,000 ° C.
  • the desired tensile limits are, as Table 2 shows, over 20 kp / mm, which means that according to this state of the art the production of age-resistant steel strips with maximum cold formability has not yet been satisfactorily resolved, and this known method in particular also fulfills the wishes for exclusively Use of continuous production processes with increased economy and improved properties of the finished products, differentiated according to the respective deformation process, material stresses and characteristics not met.
  • the finish hot rolling is preferably above a 3.
  • This AI-calmed steel has a low alloy content. It was preheated in comparative example 1 as a prior art slab at 1,270 ° C. and hot-rolled in a conventional manner with a final temperature of 920 ° C. and cold-rolled and annealed and dressed in a recrystallizing manner. Examples 1 and 2 show the effects of reduced preheating and roll temperatures. The material properties for the high preheating and final roll temperatures are plotted in the left half of the fields. The mechanical properties for the variant with high preheating and final roll temperature in Example 1, ie proof strength and elongation at break, are no longer sufficient for very demanding applications. The same characteristic values are shown in the right half of the corresponding fields when the cold strip is produced according to the invention.
  • the slab was first preheated to a temperature of 1,100 ° C and then the strip was cooled between the preliminary and finishing stages, so that the strip emerged from the last finishing stand at 800 ° C.
  • the percentage decrease in thickness of the strip after passing through the transition temperature still reached 40%.
  • Cold strip produced from this hot strip despite the low alloying effort, achieved such favorable values of yield strength, elongation at break and strengthening exponent that these products can also be used for the most demanding purposes using stretch drawing and folding.
  • the characteristic value of the vertical anisotropy r m with 1.3 is not sufficient for the production of complicated deep-drawn parts.
  • the combination according to the invention of the process step mentioned leads te to the effect that cold-rolled steel strips can be produced more reliably with improved productivity and with improved cold formability specifically for certain purposes.

Abstract

The steel strip is produced by hot strip-rolling, cold-rolling, recrystallising annealing and subsequent dressing. To be able exclusively to use continuous production processes having improved economics and at the same time to obtain improved properties of the finished products, differentiated according to the particular deformation processes, material loadings and parameters, it is proposed according to the invention to cast steels (data in percent by mass) having max. 0.06% C max. 0.10% Si max. 0.40% Mn max. 0.03% P max. 0.03% S max. 0.01% N at least one of the five elements from the following group 0- 0.10% Al 0- 0.006% B 0- 0.20% Ti 0 -0.20% Nb 0 -0.20% V impurities due to the smelting, the remainder being iron, to give ingots, to heat these before hot-rolling to a temperature of at most 1200 DEG C, to roll them out, reel them and then to recrystallisation- anneal them to yield strengths of not more than 200 N/mm<2>.

Description

Die Erfindung betrifft ein Verfahren zum Herstellen eines alterungsbeständigen Bandstahles mit hoher Kaltumformbarkeit.The invention relates to a method for producing an aging-resistant steel strip with high cold formability.

Kaltgewalztes Stahlband wird vielfach zur Herstellung von kaltumgeformten Erzeugnissen verwendet. Je nach Art des Umformverfahrens sind unterschiedliche Eigenschaften (Kennwerte) erforderlich, wobei in allen Fällen hoher Verformung niedrige Dehngrenzen und hohe Bruchdehnungswerte vorteilhaft sind. Außerdem wird für Streckziehvorgänge zusätzlich ein hoher Verfestigungsexponent nm angestrebt und für Tiefziehbeanspruchung, speziell bei Herstellung komplizierter Teile z. B. von Automobilkarosserien, sollte zusätzlich der Wert der senkrechten Anisotropie rm möglichst hoch sein.Cold rolled steel strip is widely used for the production of cold formed products. Depending on the type of forming process, different properties (characteristic values) are required, whereby in all cases of high deformation, low yield strengths and high elongation at break values are advantageous. In addition, a high strengthening exponent n m is also sought for stretch-drawing processes and for deep-drawing stress, especially when producing complicated parts, for. B. of automobile bodies, the value of the vertical anisotropy r m should also be as high as possible.

In der EP-A-108 268 wird ein Verfahren zur Herstellung von kaltgewalztem Band mit höchster Tiefziehbarkeit beschrieben, welches zwar als eine Maßnahme die Anwendung niedriger Brammenvorwärmtemperaturen unter 1 170 ° C enthält, jedoch ist der Gegenstand dieser Druckschrift auf IF-Stahl mit geringsten C-Gehalten von max. 0,007 % C und die Erfordernis einer Zugabe von Ti und Niob beschränkt. Die günstige Wirkung der niedrigen Vorwärmtemperaturen ist an das Vorhandensein von (Ti.Nb)C gebunden.EP-A-108 268 describes a process for the production of cold-rolled strip with the highest deep-drawability, which contains the use of low slab preheating temperatures below 1170 ° C. as a measure, but the subject of this document is IF steel with the lowest C - held by max. 0.007% C and the need to add Ti and niobium is limited. The favorable effect of the low preheating temperatures is linked to the presence of (Ti.Nb) C.

Die DE-OS 31 38 302 beschreibt ein Verfahren zur Herstellung von kaltgewalztem Bandstahl hoher Festigkeit aus einem Stahl, der einen hohen Phosphorgehalt von 0,05 bis 0,10 Gew.-% hat. Dabei wird eine Erwärmung der Stahlbrammen auf höchstens 1.200 ° C bzw. in den Bereich 1.200 bis 1.000 °C vorgeschlagen. Die angestrebten Dehngrenzen liegen, wie Tab. 2 belegt, über 20 kp/mm, was bedeutet, daß nach diesem Stand der Technik die Herstellung alterungsbeständiger Stahlbänder mit höchster Kaltumformbarkeit jedoch noch nicht befriedigend gelöst ist, wobei auch dieses bekannte Verfahren insbesondere die Wünsche nach ausschließlicher Verwendung kontinuierlicher Produktionsverfahren mit erhöhter Wirtschaftlichkeit und nach verbesserten Eigenschaften der Fertigprodukte, differenziert nach den jeweiligen Verformungsverfahren, Werkstoffbeanspruchungen und -kennwerten nicht erfüllt. Im übrigen ist das Fertigwarmwalzen oberhalb A3 bevorzugt.DE-OS 31 38 302 describes a process for producing cold-rolled high-strength steel strip from a steel which has a high phosphorus content of 0.05 to 0.10% by weight. It is proposed that the steel slabs be heated to a maximum of 1,200 ° C or in the range 1,200 to 1,000 ° C. The desired tensile limits are, as Table 2 shows, over 20 kp / mm, which means that according to this state of the art the production of age-resistant steel strips with maximum cold formability has not yet been satisfactorily resolved, and this known method in particular also fulfills the wishes for exclusively Use of continuous production processes with increased economy and improved properties of the finished products, differentiated according to the respective deformation process, material stresses and characteristics not met. Incidentally, the finish hot rolling is preferably above a 3.

Von daher liegt der Erfindung die Aufgabe zugrunde, ein Verfahren zum Herstellen eines alterungsbeständigen kaltgewalzten Stahlbandes, das höchste Kaltumformbarkeitseigenschaften aufweist, zu schaffen, ohne daß eine Vakuumbehandlung oder der Zusatz von Legierungselementen wie Titan, Niob oder Vanadium notwendig ist.It is therefore an object of the invention to provide a method for producing an aging-resistant cold-rolled steel strip which has the highest cold formability properties, without the need for vacuum treatment or the addition of alloying elements such as titanium, niobium or vanadium.

Diese Aufgabe wird durch die im kennzeichnenden Teil des Anspruchs 1 angegebenen Maßnahmen gelöst.This object is achieved by the measures specified in the characterizing part of claim 1.

Zweckmäßige und vorzugsweise Verfahrensschritte sind in den Unteransprüchen 2 bis 7 angegeben. Die verbesserte Kaltumformbarkeit wird anhand der im folgenden erörterten Beispiele 1 (vergleichsbeispiel) und 2 (erfindungsgemäßes Beispiel) belegt.Appropriate and preferably method steps are specified in subclaims 2 to 7. The improved cold formability is demonstrated using Examples 1 (comparative example) and 2 (example according to the invention) discussed below.

Die Auswirkungen der in den Ansprüchen festgelegten Maßnahmen sind anhand von in der Zeichnung dargestellten Balkendiagrammen erläutert.The effects of the measures specified in the claims are explained using the bar graphs shown in the drawing.

Der Stahl für die Beispiele 1 und 2 hat folgende Zusammensetzung:

  • C 0,02 %
  • Si 0,01 %
  • Mn 0,2 %
  • P 0,008 %
  • S 0,012 %
  • AI 0,04 %
  • N 0,003 %
The steel for Examples 1 and 2 has the following composition:
  • C 0.02%
  • Si 0.01%
  • Mn 0.2%
  • P 0.008%
  • S 0.012%
  • AI 0.04%
  • N 0.003%

Dieser AI-beruhigte Stahl weist einen geringen Legierungsgehalt auf. Er wurde im Vergleichsbeispiel 1 als Bramme nach dem Stand der Technik bei 1.270 ° C vorgewärmt und in herkömmlicher Weise warmgewalzt mit einer Endtemperatur von 920 ° C und kalt ausgewalzt sowie rekristallisierend geglüht und dressiert. Die Beispiele 1 und 2 zeigen die Auswirkungen abgesenkter Vorwärm- und Walzendtemperaturen. In der jeweils linken Hälfte der Felder sind die Werkstoffeigenschaften für die hohen Vorwärm- und Walzendtemperaturen aufgetragen. Die mechanischen Eigenschaften für die Variante mit hoher Vorwärm- und Walzendtemperatur im Beispiel 1, i. e. Dehngrenze und Bruchdehnung genügen nicht mehr für sehr anspruchsvolle Verwendungszwecke. In der rechten Hälfte der entsprechenden Felder sind die gleichen Kennwerte bei erfindungsgemäßer Herstellung des Kaltbandes dargestellt. Die Bramme wurde zunächst auf eine Temperatur von 1.100 ° C vorgewärmt und dann das Band zwischen Vor- und Fertigstaffel gekühlt, so daß das Band aus dem letzten Fertiggerüst mit 800 °C austrat. Die prozentuale Dickenabnahme des Bandes nach Durchlaufen der Umwandlungstemperatur erreichte noch 40 %. Aus diesem Warmband hergestelltes Kaltband erreichte trotz des geringen Legierungsaufwandes so günstige Werte von Dehngrenze, Bruchdehnung und Verfestigungsexponent, daß diese Erzeugnisse auch für anspruchsvollste Verwendungszwecke unter Einsatz von Streckziehen und Abkanten eingesetzt werden können. Allerdings ist der Kennwert der senkrechten Anisotropie rm mit 1,3 nicht ausreichend für die Herstellung komplizierter Tiefziehteile.This AI-calmed steel has a low alloy content. It was preheated in comparative example 1 as a prior art slab at 1,270 ° C. and hot-rolled in a conventional manner with a final temperature of 920 ° C. and cold-rolled and annealed and dressed in a recrystallizing manner. Examples 1 and 2 show the effects of reduced preheating and roll temperatures. The material properties for the high preheating and final roll temperatures are plotted in the left half of the fields. The mechanical properties for the variant with high preheating and final roll temperature in Example 1, ie proof strength and elongation at break, are no longer sufficient for very demanding applications. The same characteristic values are shown in the right half of the corresponding fields when the cold strip is produced according to the invention. The slab was first preheated to a temperature of 1,100 ° C and then the strip was cooled between the preliminary and finishing stages, so that the strip emerged from the last finishing stand at 800 ° C. The percentage decrease in thickness of the strip after passing through the transition temperature still reached 40%. Cold strip produced from this hot strip, despite the low alloying effort, achieved such favorable values of yield strength, elongation at break and strengthening exponent that these products can also be used for the most demanding purposes using stretch drawing and folding. However, the characteristic value of the vertical anisotropy r m with 1.3 is not sufficient for the production of complicated deep-drawn parts.

Wie aus den vorstehenden Ausführungen und den Beispielen ersichtlich, führt die erfindungsgemäße Kombination der genannten Verfahrensschritte dahin, daß mit verbesserter Produktivität kaltgewalzte Stahlbänder zuverlässiger und mit für bestimmte Verwendungszwecke gezielt verbesserter Kaltumformbarkeit hergestellt werden können.As can be seen from the above explanations and the examples, the combination according to the invention of the process step mentioned leads te to the effect that cold-rolled steel strips can be produced more reliably with improved productivity and with improved cold formability specifically for certain purposes.

Gegenüber dem erhöhten Energiebedarf beim Warmwalzen überwiegen die Vorteile des erfindungsgemäßen Verfahrens. Es seien hierfür nur einige Beispiele genannt:

  • - kürzere Durchsatzzeiten und damit erhöhte Leistung der Ofenanlage für die Brammenvorwärmung,
  • - geringere Verzunderung, also höheres Gewichtsausbringen,
  • - gezielte Kombination der Werkstoffkennwerte für unterschiedliche Kaltumformverfahren,
  • - gesteigerter Einsatz von leistungssteigernden kontinuierlichen Verfahrensschritten sämtlicher Arbeitsgänge.
The advantages of the method according to the invention outweigh the increased energy requirements during hot rolling. Here are just a few examples:
  • - shorter throughput times and thus increased performance of the furnace system for the slab preheating,
  • - less scaling, i.e. higher weight output,
  • - targeted combination of material properties for different cold forming processes,
  • - Increased use of performance-enhancing continuous process steps in all work steps.

Claims (7)

1. Process for manufacturing non-aging steel strip having a high cold formability by hot strip rolling, cold rolling, annealing in a recrystallising manner and subsequent finishing, wherein steel (details in percentage of mans) having
max. 0.06% C
max. 0.10% Si
max. 0.40% Mn
max. 0.03% P
max. 0.03% S
max. 0.01% N
at least one of the elements of the following group
0 - 0.10% AI
0 - 0.006% B
impurities caused by smelting
Residual iron
is cast into ingots, heated prior to hot rolling to temperatures of 1000 to maximum 1,200 ° C and finished hot rolled at a temperature below A3, wherein the reduction in thickness below A3 amounts to at least 35% of the thickness when passing through A3, drawn, cold rolled and subsequently annealed in a recrystallising manner to a yield strength of a maximum 200 N/mm2.
2. Process as claimed in claim 1 characterised in that the steel comprises a max. 0.05% Si.
3. Process as claimed in claims 1 and 2, characterised in that the steel comprises a maximum of 0.006%.
4. Process as claimed in one of the preceding claims, characterised in that the steel is heated prior to hot rolling to a temperature of a maximum 1,150°C, especially to a maximum 1,100 ° C, however above 1,000 ° C.
5. Process as claimed in one or several of the preceding claims, characterised in that after the cold rolling the steel is annealed in a recrystallising manner in a continuous furnace through which the stripe is drawn.
6. Process as claimed in one or several of the preceding claims, characterised in that the steel is subjected prior to the finishing to a short over-aging treatment comprising annealing in the range between approx. 250 and 450 ° C.
7. Process as claimed in one or several of the preceding claims, characterised in that the cold rolled steel is annealed continuously and subsequently, especially directly following, is provided in the melt with a metallic coating.
EP86109521A 1985-08-10 1986-07-11 Process for manufacturing non-aging steel strip having a high cold formability Expired - Lifetime EP0216044B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT86109521T ATE104362T1 (en) 1985-08-10 1986-07-11 PROCESS FOR PRODUCTION OF AN AGING-RESISTANT STEEL STRIP WITH HIGH COLD FORMABILITY.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19853528782 DE3528782A1 (en) 1985-08-10 1985-08-10 METHOD FOR PRODUCING AN AGING-RESISTANT STRIP STEEL WITH HIGH COLD FORMABILITY
DE3528782 1985-08-10

Publications (4)

Publication Number Publication Date
EP0216044A2 EP0216044A2 (en) 1987-04-01
EP0216044A3 EP0216044A3 (en) 1989-06-14
EP0216044B1 true EP0216044B1 (en) 1994-04-13
EP0216044B2 EP0216044B2 (en) 1997-09-03

Family

ID=6278246

Family Applications (1)

Application Number Title Priority Date Filing Date
EP86109521A Expired - Lifetime EP0216044B2 (en) 1985-08-10 1986-07-11 Process for manufacturing non-aging steel strip having a high cold formability

Country Status (3)

Country Link
EP (1) EP0216044B2 (en)
AT (1) ATE104362T1 (en)
DE (2) DE3528782A1 (en)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0496416A1 (en) * 1991-01-25 1992-07-29 Nkk Corporation Nickel alloy electroplated cold-rolled steel sheet excellent in press-formability and phosphating-treatability and method for manufacturing same
WO2000014288A1 (en) * 1998-09-08 2000-03-16 Thyssen Krupp Stahl Ag Method for producing cold-rolled bands or sheets

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3422612B2 (en) * 1996-01-19 2003-06-30 Ｊｆｅスチール株式会社 Manufacturing method of ultra low carbon cold rolled steel sheet
DE19701443A1 (en) * 1997-01-17 1998-07-23 Thyssen Stahl Ag Cold rolled steel sheet or strip with good formability used for car parts production
DE19740148C1 (en) * 1997-09-12 1999-07-15 Thyssenkrupp Stahl Ag Process for the manufacture of dent-resistant enamelled components made of age-sensitive steel
DE19834361A1 (en) * 1998-07-30 2000-02-03 Schaeffler Waelzlager Ohg Precision deep-drawn case-hardened component, especially a roller bearing and motor component e.g. a needle bearing, sleeve or bush, is made from a cold rolled strip of steel with specified titanium, nitrogen and low aluminum contents
DE19946889C1 (en) * 1999-09-30 2000-11-09 Thyssenkrupp Stahl Ag Aging resistant aluminum-killed steel strip, for manufacturing cold formed components e.g. bodywork parts, is produced by subjecting rolled strip to continuous annealing, hot coiling, cooling to room temperature and skin pass rolling
DE10020118B4 (en) 2000-04-22 2009-11-12 Schaeffler Kg Method for verifying sealability of selected exhaust valve of selected cylinder in internal combustion engine in motor vehicle, involves concluding sealability of valve based on measured values of lambda sensor in one of exhaust gas strands
CN107099648A (en) * 2017-06-27 2017-08-29 中国航空工业集团公司沈阳飞机设计研究所 The structure property homogenization heat treatment method of the steel of laser deposition molding A 100

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
NL7412582A (en) * 1974-09-24 1976-03-26 Armco Steel Corp PROCESS FOR THE MANUFACTURE OF COLD ROLLED AND BLAST STEEL SHEET.
JPS5849627B2 (en) * 1979-02-27 1983-11-05 川崎製鉄株式会社 Method for producing non-temporal cold-rolled steel sheet
JPS56166330A (en) * 1980-04-25 1981-12-21 Nippon Steel Corp Manufacture of cold rolled steel plate for deep drawing by continuous annealing
JPS5857492B2 (en) * 1980-09-25 1983-12-20 新日本製鐵株式会社 Manufacturing method of high-strength cold-rolled steel sheet for automobiles
DE3170723D1 (en) * 1981-08-25 1985-07-04 Nippon Steel Corp Dual-purpose plant for producing cold rolled steel sheet and hot-dip galvanized steel sheet
JPS6045689B2 (en) * 1982-02-19 1985-10-11 川崎製鉄株式会社 Method for manufacturing cold rolled steel sheet with excellent press formability
US4504326A (en) * 1982-10-08 1985-03-12 Nippon Steel Corporation Method for the production of cold rolled steel sheet having super deep drawability
US4473411A (en) * 1983-07-20 1984-09-25 Armco Inc. Process of making aluminum killed low manganese deep drawing steel

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0496416A1 (en) * 1991-01-25 1992-07-29 Nkk Corporation Nickel alloy electroplated cold-rolled steel sheet excellent in press-formability and phosphating-treatability and method for manufacturing same
US5336567A (en) * 1991-01-25 1994-08-09 Nkk Corporation Nickel alloy electroplated cold-rolled steel sheet excellent in press-formability and phosphating-treatability
US5456816A (en) * 1991-01-25 1995-10-10 Nkk Corporation Nickel alloy electroplated cold-rolled steel sheet excellent in press-formability and phosphating-treatability and method for manufacturing same
WO2000014288A1 (en) * 1998-09-08 2000-03-16 Thyssen Krupp Stahl Ag Method for producing cold-rolled bands or sheets
AU749783B2 (en) * 1998-09-08 2002-07-04 Thyssen Krupp Stahl Ag Method for producing cold-rolled bands or sheets
US6582537B1 (en) 1998-09-08 2003-06-24 Thyssen Krupp Stahl Ag Method for producing cold-rolled bands or sheets

Also Published As

Publication number Publication date
DE3528782A1 (en) 1987-02-19
EP0216044A2 (en) 1987-04-01
DE3689781D1 (en) 1994-05-19
DE3528782C2 (en) 1990-06-13
EP0216044B2 (en) 1997-09-03
EP0216044A3 (en) 1989-06-14
ATE104362T1 (en) 1994-04-15

Similar Documents

Publication Publication Date Title
EP1918406B1 (en) Process for manufacturing steel flat products from boron microalloyed multi phase steel
EP1918402B1 (en) Process for manufacturing steel flat products from a steel forming a complex phase structure
EP1918403B1 (en) Process for manufacturing steel flat products from a steel forming martensitic structure
EP0352597B1 (en) Process for producing hot-rolled strip or heavy plates
DE19622164C1 (en) Cold rolled steel sheet with good drawing properties
EP1194600B1 (en) Method of producing non-grain-oriented electrical sheet
EP1263993B1 (en) Method for producing non grain-oriented electric sheets
DE2334399A1 (en) METHOD OF MANUFACTURING NON-ORIENTED ELECTRICAL SHEET
DE1433817A1 (en) Process for the manufacture of non-aging iron sheets with a particularly low carbon content
EP1918405B1 (en) Process for manufacturing steel flat products from silicon alloyed multi phase steel
EP0216044B1 (en) Process for manufacturing non-aging steel strip having a high cold formability
EP0181583B1 (en) Method of making a dual-phase hot-rolled steel strip
DE2433665B2 (en) Process for the production of high-strength sheet metal
EP1918404B1 (en) Process for manufacturing steel flat products from aluminium alloyed multi phase steel
DE2503988C2 (en) Method of making a cold rolled steel strip
DE10055338C1 (en) Production of cold strip comprises hot rolling pre-material produced from steel, cold rolling hot strip to form cold strip, annealing at temperature which is lower than recrystallization temperature, cold deforming, and further annealing
WO2002048410A1 (en) Method for the production of hot strip or sheet from a micro-alloyed steel
DE3304064C2 (en)
DE3234574C2 (en)
DE2348062C3 (en) Process for the production of a non-calmed, age-resistant deep-drawing steel
DE19840788C2 (en) Process for producing cold-rolled strips or sheets
DE2810188A1 (en) Heat treating continuously cast and rolled aluminium alloy strip - consists of annealing to obtain good combination of strength and deep drawing properties
EP1411140B1 (en) Process for manufacturing of cold-rolled steel strips or sheets having excellent formability
EP4206336A1 (en) Plate and thermomechanical processing method of raw material for producing a plate
DD144565A1 (en) ALUMINUM ALLOYING WITH SPECIAL FORMING PROPERTIES AND METHOD FOR PROCESSING THIS ALLOY

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A2

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

ITCL It: translation for ep claims filed

Representative=s name: RICCARDI SERGIO & CO.

EL Fr: translation of claims filed
TCNL Nl: translation of patent claims filed
PUAL Search report despatched

Free format text: ORIGINAL CODE: 0009013

AK Designated contracting states

Kind code of ref document: A3

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

17P Request for examination filed

Effective date: 19890812

17Q First examination report despatched

Effective date: 19910417

RAP1 Party data changed (applicant data changed or rights of an application transferred)

Owner name: KRUPP HOESCH STAHL AG

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

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

REF Corresponds to:

Ref document number: 104362

Country of ref document: AT

Date of ref document: 19940415

Kind code of ref document: T

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

Effective date: 19940419

REF Corresponds to:

Ref document number: 3689781

Country of ref document: DE

Date of ref document: 19940519

ET Fr: translation filed
ITF It: translation for a ep patent filed

Owner name: UFFICIO BREVETTI RICCARDI & C.

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

Ref country code: AT

Effective date: 19940711

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

Ref country code: SE

Effective date: 19940712

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

Ref country code: GB

Effective date: 19940713

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

Ref country code: LU

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

Effective date: 19940731

Ref country code: LI

Effective date: 19940731

Ref country code: CH

Effective date: 19940731

Ref country code: BE

Effective date: 19940731

PLBI Opposition filed

Free format text: ORIGINAL CODE: 0009260

26 Opposition filed

Opponent name: THYSSEN STAHL AG

Effective date: 19940927

NLR1 Nl: opposition has been filed with the epo

Opponent name: THYSSEN STAHL AG

BERE Be: lapsed

Owner name: KRUPP HOESCH STAHL A.G.

Effective date: 19940731

EUG Se: european patent has lapsed

Ref document number: 86109521.4

Effective date: 19950210

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

Ref country code: NL

Effective date: 19950201

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 19940713

NLV4 Nl: lapsed or anulled due to non-payment of the annual fee
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Effective date: 19950331

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

EUG Se: european patent has lapsed

Ref document number: 86109521.4

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

PLAW Interlocutory decision in opposition

Free format text: ORIGINAL CODE: EPIDOS IDOP

APAE Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOS REFNO

APAC Appeal dossier modified

Free format text: ORIGINAL CODE: EPIDOS NOAPO

APAC Appeal dossier modified

Free format text: ORIGINAL CODE: EPIDOS NOAPO

APAC Appeal dossier modified

Free format text: ORIGINAL CODE: EPIDOS NOAPO

PLAW Interlocutory decision in opposition

Free format text: ORIGINAL CODE: EPIDOS IDOP

PUAH Patent maintained in amended form

Free format text: ORIGINAL CODE: 0009272

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: PATENT MAINTAINED AS AMENDED

27A Patent maintained in amended form

Effective date: 19970903

AK Designated contracting states

Kind code of ref document: B2

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

REG Reference to a national code

Ref country code: CH

Ref legal event code: AEN

Free format text: AUFRECHTERHALTUNG DES PATENTES IN GEAENDERTER FORM

EN Fr: translation not filed
PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20020711

Year of fee payment: 17

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

Ref country code: DE

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

Effective date: 20040203

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

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED.

Effective date: 20050711

APAH Appeal reference modified

Free format text: ORIGINAL CODE: EPIDOSCREFNO