EP1065286B1 - Tole d'acier à basse teneur en aluminium pour emballage - Google Patents

Tole d'acier à basse teneur en aluminium pour emballage Download PDF

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Publication number
EP1065286B1
EP1065286B1 EP00401869A EP00401869A EP1065286B1 EP 1065286 B1 EP1065286 B1 EP 1065286B1 EP 00401869 A EP00401869 A EP 00401869A EP 00401869 A EP00401869 A EP 00401869A EP 1065286 B1 EP1065286 B1 EP 1065286B1
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EP
European Patent Office
Prior art keywords
strip
temperature
steel
low
annealing
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.)
Revoked
Application number
EP00401869A
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German (de)
English (en)
French (fr)
Other versions
EP1065286A1 (fr
Inventor
Mohamed Bouzekri
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.)
Sollac SA
Original Assignee
Sollac SA
Lorraine de Laminage Continu SA SOLLAC
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Publication date
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Application filed by Sollac SA, Lorraine de Laminage Continu SA SOLLAC filed Critical Sollac SA
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C21D8/0436—Cold 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
    • 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
    • C21D8/0447—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 heat treatment
    • C21D8/0468—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 heat treatment between cold rolling steps
    • 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
    • C21D8/0447—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 heat treatment
    • C21D8/0473—Final recrystallisation annealing

Definitions

  • the present invention relates to the field of steels for application in the field of metal packaging, food, non food or industrial.
  • the thicknesses of the steel sheets for packaging vary from 0.12 mm to 0.25 mm for the majority of uses, but may achieve greater thicknesses, up to 0.49 mm for very specific applications. This is for example the case of some non-food packaging, such as certain aerosols, or certain industrial packaging. They can also go down up to 0.08 mm, for example in the case of food trays.
  • Steel sheets for packaging are usually coated a metallic coating (tin, remelted or not, or chrome) on which is generally deposited an organic coating (varnish, inks, films plastics).
  • the carbon content usually targeted for this type of steel is between 0.050% and 0.080%, the manganese content included between 0.20 and 0.45%.
  • Aluminum content is controlled to be lower at 0.020% in order to give the steel sheet a microstructure improved, good inclusiveness, and consequently high mechanical characteristics.
  • the nitrogen content is also controlled and is understood between 0.008 and 0.016%. This nitrogen content is ensured by adding to the bag of calcium cyanamide during steel making, or by blowing nitrogen gas in the steel bath.
  • the known advantage of adding nitrogen is harden the steel by effect of solid solution.
  • These steel sheets are produced by cold rolling a hot strip, with a cold rolling rate of between 75% and more 90%, followed by continuous annealing at a temperature between 640 and 700 ° C, and a second cold rolling with an elongation rate during of this second cold rolling variable between 2% and 45% depending on the level of maximum breaking strength Rm targeted.
  • the present invention aims to provide a steel sheet to low aluminum content for packaging that presents a rate A higher elongation than% low steels state-of-the-art aluminum, at maximum resistance to equivalent break.
  • the invention also relates to a steel sheet with low aluminum content comprising by weight between 0.050 and 0.080% of carbon, between 0.25 and 0.40% of manganese, less than 0.020% of aluminum, between 0.010 and 0.014 % nitrogen, the rest being iron and unavoidable residual impurities, manufactured according to the above process, characterized in that it has, in the aged state, an elongation rate A% satisfying the relationship: (750 - Rm) / 16.5 ⁇ A% ⁇ (850 - Rm) / 17.5 Rm being the maximum breaking strength of the steel, expressed in MPa.
  • the steel has COTTRELL atmospheres and / or epsilon carbides precipitated at low temperature, and has a number of grains per mm 2 greater than 30,000.
  • Figures 1 and 2 are diagrams showing the influence of the annealing temperature on the maximum breaking strength Rm.
  • Figure 3 is a diagram showing the influence of speed cooling on the maximum breaking strength Rm.
  • Figure 4 is a diagram showing the influence of speed cooling on the maximum breaking strength Rm and the rate elongation A%.
  • Figure 5 is a diagram showing the influence of speed cooling on hardness HR30T.
  • Figure 6 is a diagram showing the influence of processing thermal at low temperature on the maximum breaking strength Rm.
  • Figure 7 is a diagram showing the influence of processing thermal at low temperature on and the elongation rate A%.
  • Figure 8 is a diagram showing the influence of plastic deformation in elongation on the maximum breaking strength Rm.
  • the coil in the first column, we identified the coil; in the second to fifth columns, the contents of the main constituents of importance are indicated in 10 -3 % by weight.
  • the sixth to eighth columns relate to the hot rolling conditions: in the sixth column, the end of hot rolling temperature is indicated; in the seventh column, the winding temperature; in the eighth column, the thickness of the hot strip.
  • columns nine and ten relate to the cold rolling conditions: in the ninth column, the reduction rate of the cold rolling is indicated and in the tenth column, the final thickness of the cold strip.
  • the annealing holding temperatures varied from 650 ° C to 800 ° C
  • the cooling rates varied from 40 ° C / s to 400 ° C / s
  • the low temperature annealing temperatures ranged from 150 to 350 ° C
  • the elongation rates on second rolling varied from 1% to 42%, with or without plastic deformation in intermediate lengthening.
  • the invention does not lie in the composition of steel, which is a low aluminum steel standard.
  • Continuously annealed renitrided low aluminum steels are generally rolled at a temperature above Ar 3 .
  • a hot winding can be carried out by practicing for example a selective winding: the temperature is higher in ends of the strip.
  • the field of Cold reduction rate ranges from 75% to over 90%.
  • Metallurgical considerations are based on the incidence of the rate of cold reduction on the microstructural state, and by way of consequence on the mechanical characteristics after recrystallization and annealing.
  • the more the cold reduction rate increases the more the temperature of the lower the recrystallization, the weaker the grains and the more Re and Rm are high.
  • the reduction rate has a very strong impact on the Lankford coefficient.
  • metal without horns In the case of requirements in terms of drawing horns, it for example, optimize the steel grade and especially the content of carbon, and the reduction rate of cold rolling with hardness or mechanical characteristics desired to obtain a metal known as “metal without horns ".
  • An important characteristic of the invention lies in the annealing temperature. It is important that the annealing temperature is higher than the point of start of pearlitic transformation Ac 1 (of the order of 720 ° C. for this type of steel).
  • cooling rate which must be greater than 100 ° C / s.
  • austenite rich in carbon
  • the rapid cooling of this austenite keeps a certain amount of carbon and nitrogen in the free state.
  • This low temperature heat treatment is to precipitate free carbon atoms as fine precipitates and dispersed of low temperature carbides and / or epsilon carbides. It allows also the segregation of free carbon and nitrogen atoms at the level dislocations to form COTTRELL atmospheres.
  • Figures 1 and 2 show the influence of the annealing at constant cooling rate (Aimed at 100 ° C / s and performed 73 to 102 ° C / s in Figure 1; Aimed at 300 ° C / s and performed 228 to 331 ° C / s on the Figure 2) on the maximum breaking strength Rm.
  • This phenomenon is glimpsed in Figure 2 on which we notice, for elongation rates greater than 10%, a decrease in the increase in maximum tensile strength Rm between the annealed sample at 750 ° C and the sample annealed at 800 ° C.
  • the strip holding time between Ac 1 and 800 ° C must be sufficient to put all the carbon corresponding to equilibrium back into solution. Maintaining for 10 seconds is sufficient to ensure this redissolution of the quantity of carbon corresponding to equilibrium for steels whose carbon content is between 0.020 and 0.035%, and maintaining beyond 2 minutes, although possible, is unnecessary and expensive.
  • Figures 3 and 4 show the influence of the speed of constant annealing temperature (750 ° C) maintained for 20 seconds.
  • the maximum tensile strength Rm of the steel is equal to around 560 MPa if the cooling rate is equal to 100 ° C / s, when it only reaches 505 MPa if the cooling speed is equal to 50 ° C / s.
  • the maximum resistance to rupture Rm decreases when the temperature of the heat treatment exceeds 300 ° C.
  • the value of Rm is only equal on average to 540 MPa, which represents a decrease of 20 MPa compared to the same steel obtained without low heat treatment temperature, unlike elongation rate during rolling at secondary cold near.
  • This decrease in Rm with the temperature of the heat treatment is due to precipitation of carbon in the form of cementite.
  • the low heat treatment temperature also increases the elongation rate A%, which thus goes from 4.8% to an average of 9%, all conditions equal by elsewhere.
  • This plastic deformation creates dislocations on which will form during heat treatment at low temperatures COTTRELL atmospheres, i.e. accumulations of atoms of free carbon and nitrogen around the dislocations generated by the plastic deformation, and / or epsilon carbides. So, following the heat treatment at low temperature, the dislocations generated by the deformation of the material will be immobilized or anchored by these COTTRELL atmospheres, which hardens the steel.
  • the tensile strength Rm of steel A increases significantly if we perform a small plastic deformation in elongation, between high temperature annealing and heat treatment at low temperature. For example, we see that for a total elongation rate equal to 15% achieved in one go after low heat treatment temperature, the value of Rm is equal to 660 MPa. However, if we performs an intermediate plastic deformation with an elongation rate equal to 1%, the total elongation rate remaining equal to 15% (which means that the rate of elongation is reduced during secondary cold rolling), the value of Rm is equal to 672 MPa. It reaches 700 MPa with a rate of intermediate plastic deformation equal to 3%.
  • This intermediate plastic deformation in elongation can be carried out by leveling under tension or by rolling.
  • Micrographic analyzes of the samples revealed that the number of grains per mm 2 is higher (more than 30,000).
  • this manufacturing process makes it possible to produce a steel with low aluminum content for packaging, comprising by weight between 0.050 and 0.080% of carbon, between 0.25 and 0.40% of manganese, less than 0.020% of aluminum, between 0.010 and 0.014% nitrogen, the rest being iron and inevitable residual impurities, which in the aged state has an elongation rate A% satisfying the relationship: (750 - Rm) / 16.5 ⁇ A% ⁇ 850 - Rm) / 17.5 Rm being the maximum breaking strength of the steel, expressed in MPa.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Laminated Bodies (AREA)
  • Wrappers (AREA)
  • Chemical Treatment Of Metals (AREA)
EP00401869A 1999-07-01 2000-06-30 Tole d'acier à basse teneur en aluminium pour emballage Revoked EP1065286B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9908419A FR2795744B1 (fr) 1999-07-01 1999-07-01 Tole d'acier a basse teneur en aluminium pour emballage
FR9908419 1999-07-01

Publications (2)

Publication Number Publication Date
EP1065286A1 EP1065286A1 (fr) 2001-01-03
EP1065286B1 true EP1065286B1 (fr) 2002-08-21

Family

ID=9547533

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00401869A Revoked EP1065286B1 (fr) 1999-07-01 2000-06-30 Tole d'acier à basse teneur en aluminium pour emballage

Country Status (10)

Country Link
US (1) US6974511B1 (pt)
EP (1) EP1065286B1 (pt)
AT (1) ATE222607T1 (pt)
BR (1) BR0002268A (pt)
CA (1) CA2314177C (pt)
DE (1) DE60000342T2 (pt)
DK (1) DK1065286T3 (pt)
ES (1) ES2180499T3 (pt)
FR (1) FR2795744B1 (pt)
PT (1) PT1065286E (pt)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102794301A (zh) * 2012-08-03 2012-11-28 莱芜市泰山冷轧板有限公司 一种冷轧电镀锡基板生产方法

Families Citing this family (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2795743B1 (fr) * 1999-07-01 2001-08-03 Lorraine Laminage Tole d'acier a basse teneur en aluminium pour emballage
FR2857980B1 (fr) * 2003-07-22 2006-01-13 Usinor Procede de fabrication de toles d'acier austenitique fer-carbone-manganese, a haute resistance, excellente tenacite et aptitude a la mise en forme a froid, et toles ainsi produites
CN102766800A (zh) * 2011-05-05 2012-11-07 上海梅山钢铁股份有限公司 一种硬质镀锡基板瓶盖用钢及其生产方法
EP2860124B2 (en) † 2012-06-06 2020-03-18 JFE Steel Corporation Three-piece can and method for producing same
DE102014112286A1 (de) * 2014-08-27 2016-03-03 Thyssenkrupp Ag Verfahren zur Herstellung eines aufgestickten Verpackungsstahls
DE102014116929B3 (de) 2014-11-19 2015-11-05 Thyssenkrupp Ag Verfahren zur Herstellung eines aufgestickten Verpackungsstahls, kaltgewalztes Stahlflachprodukt und Vorrichtung zum rekristallisierenden Glühen und Aufsticken eines Stahlflachprodukts
CN104988292B (zh) * 2015-07-08 2017-05-31 河钢集团衡水板业有限公司 一种深冲用dr材基板的生产方法

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GB1013257A (en) * 1963-05-01 1965-12-15 British Iron Steel Research Improvements in or relating to annealing
JPS5157623A (en) * 1974-11-18 1976-05-20 Nippon Kokan Kk Takaitosoyakitsukekokaseitosugureta hijikoseiomotsukochoryokureienkohanno seizohoho
JPS5827933A (ja) * 1981-08-13 1983-02-18 Kawasaki Steel Corp 連続焼鈍による耐食性に優れるｔ−３軟質ぶりき原板の製造方法
US4698102A (en) * 1984-07-09 1987-10-06 Nippon Steel Corporation Process for producing, by continuous annealing, soft blackplate for surface treatment
JP3303938B2 (ja) * 1993-04-26 2002-07-22 新日本製鐵株式会社 耐圧強度とネックドイン性に優れたｄｉ缶用表面処理原板
JP2676581B2 (ja) * 1993-07-14 1997-11-17 東洋鋼鈑株式会社 薄肉化深絞り缶用途に適した鋼板およびその製造法
JP2623432B2 (ja) * 1993-07-14 1997-06-25 東洋鋼鈑株式会社 薄肉化深絞り缶用途に適した鋼板およびその製造法
JP2668503B2 (ja) * 1993-07-14 1997-10-27 東洋鋼鈑株式会社 薄肉化深絞り缶用途に適した鋼板およびその製造法
FR2739105B1 (fr) * 1995-09-21 1998-04-30 Lorraine Laminage Procede de fabrication d'une bande metallique pour emballages et emballages metalliques obtenus par ce procede
JPH1030152A (ja) * 1997-04-04 1998-02-03 Toyo Kohan Co Ltd 薄肉化深絞り缶用途に適した鋼板およびその製造法
FR2769251B1 (fr) * 1997-10-03 1999-12-24 Lorraine Laminage Procede de fabrication d'une bande de tole d'acier pour la realisation d'emballages metalliques par emboutissage et tole d'acier obtenue

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102794301A (zh) * 2012-08-03 2012-11-28 莱芜市泰山冷轧板有限公司 一种冷轧电镀锡基板生产方法
CN102794301B (zh) * 2012-08-03 2014-07-09 莱芜市泰山冷轧板有限公司 一种冷轧电镀锡基板生产方法

Also Published As

Publication number Publication date
DE60000342D1 (de) 2002-09-26
CA2314177C (fr) 2010-04-20
ES2180499T3 (es) 2003-02-16
BR0002268A (pt) 2001-03-13
FR2795744A1 (fr) 2001-01-05
DE60000342T2 (de) 2004-05-13
EP1065286A1 (fr) 2001-01-03
DK1065286T3 (da) 2002-12-23
ATE222607T1 (de) 2002-09-15
CA2314177A1 (fr) 2001-01-01
US6974511B1 (en) 2005-12-13
FR2795744B1 (fr) 2001-08-03
PT1065286E (pt) 2002-12-31

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