EP0754770A1 - Method of producing a thin steel strip having improved deep-drawing properties - Google Patents
Method of producing a thin steel strip having improved deep-drawing properties Download PDFInfo
- Publication number
- EP0754770A1 EP0754770A1 EP96401347A EP96401347A EP0754770A1 EP 0754770 A1 EP0754770 A1 EP 0754770A1 EP 96401347 A EP96401347 A EP 96401347A EP 96401347 A EP96401347 A EP 96401347A EP 0754770 A1 EP0754770 A1 EP 0754770A1
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- European Patent Office
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- cold rolling
- strip
- reduction rate
- sheet metal
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Classifications
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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
- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
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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
- 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
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- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-rolling
Definitions
- the present invention relates to a method of manufacturing a strip of thin sheet metal with improved drawability having good capacity for expanding deformation and for shrinking deformation, as well as a thin sheet metal with improved stampability obtained by this method.
- Steels for stamping either shrinking in the context of steels for packaging, or expanding in the context of steels for example for cars, must have a certain number of particular characteristics to allow their shaping.
- the work hardening coefficient n must be as high as possible. Indeed, this work hardening coefficient defines the ability of the material to deform in expansion and, the higher this coefficient, the better the material deforms in expansion.
- the anisotropy coefficient r ⁇ in the direction where it is lowest and the average anisotropy coefficient r ⁇ must also be raised. Indeed, the significant cold work hardening which the sheet metal strip undergoes during rolling results, after annealing, in the formation of crystallographic textures leading to an anisotropy of the mechanical properties. Its influence on the elastic limit Re, the tensile strength Rm and the elongation percent at break A% is relatively weak, but it is not the same for the thinning of the sheet during stresses suffered by the sheet during shaping.
- This coefficient r ⁇ represents the thinning capacity of the sheet and to guarantee the best drawing conditions, that is to say a good flow of the metal in all directions, a Lankford coefficient is required r ⁇ as high as possible.
- anisotropy coefficient r ⁇ in the direction where it is the lowest r mini is as high as possible, which ensures that in all directions of stress, the metal does not go too thin.
- the Young's modulus must also be as high as possible, and a steel is all the more stampable as it develops these properties.
- This type of steel has good drawing characteristics.
- the steel thus produced is hot rolled, cold rolled with a reduction rate of 50%, then annealed at 750 ° C for 20 seconds, cold rolled with a reduction rate of 77% and annealed a second time at 870 ° C for 20 seconds.
- This type of steel sheet has a Lankford coefficient r ⁇ high but does not necessarily have the other properties necessary for good stamping, and it is extremely expensive to carry out essentially because of the low carbon content necessary to obtain this Lankford coefficient, as well as the high temperatures of the annealing
- the object of the present invention is to propose a method for manufacturing a strip of thin sheet metal with improved stampability having a good ability both in expanding deformation and in shrinking deformation, as well as improved elongation at break. , and which is economical to produce.
- the present invention also relates to a strip of thin sheet metal having a good drawing ability obtained by the process according to the above characteristics.
- the invention relates to a strip of thin sheet steel of improved stampability, that is to say having a low yield strength, a high Lankford coefficient greater than 2, preferably 2.4 in all directions of the sheet, significant consolidation, significant ductility and a high Young's modulus greater than 23,000 kg / mm 2 .
- a steel is first produced, in a known manner, for example using a steelworks converter, the composition of which in thousandths of a percent is as follows: carbon ⁇ 20 silicon ⁇ 500 manganese ⁇ 1000 phosphorus ⁇ 100 sulfur ⁇ 50 aluminum ⁇ 100 nitrogen ⁇ 10 and none, one or more of the following: titanium ⁇ 150 niobium ⁇ 150 boron ⁇ 5 the rest being iron and residuals from the production process.
- the steel has the following composition, in thousandths of a percent: carbon from 2 to 20 silicon from 100 to 500 manganese from 0 to 1000 phosphorus from 50 to 100 sulfur from 0 to 50 aluminum from 0 to 100 nitrogen from 2 to 8 and none, one or more of the following: titanium from 0 to 150 niobium from 10 to 50 boron from 0 to 2 the rest being iron and residuals from the production process.
- the steel thus produced is then poured into slabs and then hot rolled.
- the hot rolled strip is then cold rolled with a reduction rate greater than 20%.
- the strip thus cold-rolled is then subjected to annealing at a temperature between the temperature for restoring the steel and 920 ° C., preferably between the temperature for restoring the steel and its recrystallization temperature.
- Annealing can either be basic annealing or continuous annealing.
- a second cold rolling is then carried out with a reduction rate greater than 20% by imparting a determined roughness to the sheet metal strip.
- a second annealing is carried out at a temperature higher than the recrystallization temperature of the steel.
- the Applicant has found that it is possible to increase the value of the Lankford coefficient r ⁇ of the sheet so that it is greater than 2, preferably 2.4 when the temperature of the first annealing takes place at a temperature between the temperature for restoring the steel and its recrystallization temperature, preferably at a temperature equal to the steel restoration temperature plus 40 to 60 ° C.
- the first scenario in which the reduction rate of the first cold rolling is low, while being greater than 20%, preferably of the order of 35 to 50%, and the reduction rate of the second rolling is high , preferably of the order of 65 to 75%.
- the second scenario in which the reduction rate of the first cold rolling is high, preferably of the order of 65 to 75% and the reduction rate of the second cold rolling is low, while being greater than 20 %, preferably of the order of 35 to 50%.
- the printed roughness is such that the average roughness Ra is between 0.9 and 1.7 microns.
- the average roughness Ra is between 1.2 and 1.7 to promote stamping. But if one wishes to obtain a more shiny appearance to the sheet, while retaining good stampability, the sheet is printed with an average roughness Ra of between 0.9 and 1.4 microns.
- This operation makes it possible, by eliminating the skin-pass operation, to guarantee a high Lankford coefficient greater than 2, preferably 2.4 and a low elastic limit because the skin-pass operation has the consequence of increasing the yield strength of the metal, and degrading the work hardening coefficient not ⁇ .
- the fact of being free from the skin-pass operation makes it possible to omit a step in the manufacture of the sheet metal strip and consequently reduces the cost thereof.
- steels A and B are steels according to the invention and steel C corresponds to a composition according to the state of the art.
- the restoration temperature of steel A which was produced with a first base annealing, is equal to 450 ° C. and its recrystallization temperature is equal to 680 ° C.
- the restoration temperature of steel B which was produced with a first continuous annealing, is equal to 450 ° C. and its recrystallization temperature is equal to 630 ° C.
- Each of the three types of steel was then subjected to different rolling and annealing treatments and several sheet metal strips less than 1 mm thick were thus produced.
- the steel of the invention makes it possible to obtain, compared with steel C of the prior art, a significant gain in terms of ductility and in terms of drawability.
Abstract
Description
La présente invention concerne un procédé de fabrication d'une bande de tôle mince à emboutissabilité améliorée ayant une bonne aptitude à la déformation en expansion et à la déformation en rétreint, ainsi qu'une tôle mince à emboutissabilité améliorée obtenue par ce procédé.The present invention relates to a method of manufacturing a strip of thin sheet metal with improved drawability having good capacity for expanding deformation and for shrinking deformation, as well as a thin sheet metal with improved stampability obtained by this method.
Les aciers pour emboutissage, soit en rétreint dans le cadre des aciers pour emballage, soit en expansion dans le cadre des aciers par exemple pour automobile, doivent présenter un certain nombre de caractéristiques particulières pour permettre leur mise en forme.Steels for stamping, either shrinking in the context of steels for packaging, or expanding in the context of steels for example for cars, must have a certain number of particular characteristics to allow their shaping.
Leur limite d'élasticité Re doit être le plus faible possible pour un niveau de résistance à la rupture Rm donné, afin de faciliter la déformation.Their elastic limit Re must be as low as possible for a given level of breaking strength Rm, in order to facilitate deformation.
Le coefficient d'écrouissage n doit être le plus élevé possible. En effet ce coefficient d'écrouissage définit l'aptitude du matériau à se déformer en expansion et, plus ce coefficient est élevé, mieux le matériau se déforme en expansion.The work hardening coefficient n must be as high as possible. Indeed, this work hardening coefficient defines the ability of the material to deform in expansion and, the higher this coefficient, the better the material deforms in expansion.
Le coefficient d'anisotropie rϕ dans la direction où il est le plus faible et le coefficient d'anisotropie moyen
Pour mesurer cette anisotropie, on utilise le rapport rϕ entre la déformation rationnelle en largeur d'une éprouvette, lors d'un essai de traction, et sa déformation rationnelle en épaisseur, ou ϕ représente l'angle entre la direction de traction de l'éprouvette et la direction de laminage de la tôle.To measure this anisotropy, we use the ratio r ϕ between the rational deformation in width of a test piece, during a tensile test, and its rational deformation in thickness, where ϕ represents the angle between the direction of traction of l 'specimen and the direction of rolling of the sheet.
L'anisotropie moyenne d'un acier est déterminée par le coefficient d'anisotropie moyen
Ce coefficient
Il est également important que le coefficient d'anisotropie rϕ dans la direction où celui-ci est le plus faible rmini soit le plus élevé possible, ce qui permet de garantir que dans toutes les directions de sollicitation, le métal ne va pas trop s'amincir.It is also important that the anisotropy coefficient r ϕ in the direction where it is the lowest r mini is as high as possible, which ensures that in all directions of stress, the metal does not go too thin.
Le caractère élevé de ces deux coefficients rmini et
Il est également important que l'allongement pour cent à la rupture A% soit élevé ce qui traduit une ductilité importante du matériau.It is also important that the elongation percent at break A% be high, which translates into significant ductility of the material.
Enfin, le module de Young doit également être le plus élevé possible, et un acier est d'autant plus emboutissable qu'il développe ces propriétés.Finally, the Young's modulus must also be as high as possible, and a steel is all the more stampable as it develops these properties.
Il est connu pour ce type d'application d'utiliser des aciers standards par exemple un acier ayant la composition suivante en millième de pourcent poids :
Ce type d'acier présente de bonnes caractéristiques d'emboutissage.This type of steel has good drawing characteristics.
Il est également connu d'élaborer des aciers de manière très spécifiques pour augmenter encore les propriétés d'emboutissage, en particulier le coefficient de Lankford
Par exemple, il existe un acier dont le coefficient de Lankford
L'acier ainsi élaboré est laminé à chaud, laminé à froid avec un taux de réduction de 50%, puis recuit à 750°C pendant 20 secondes, relaminé à froid avec un taux de réduction de 77% et recuit une seconde fois à 870°C pendant 20 secondes.The steel thus produced is hot rolled, cold rolled with a reduction rate of 50%, then annealed at 750 ° C for 20 seconds, cold rolled with a reduction rate of 77% and annealed a second time at 870 ° C for 20 seconds.
Ce type de tôle d'acier présente un coefficient de Lankford
La présente invention a pour but de proposer un procédé de fabrication d'une bande de tôle mince à emboutissabilité améliorée ayant une bonne aptitude aussi bien à la déformation en expansion qu'à la déformation en rétreint, ainsi qu'un allongement à la rupture amélioré, et qui soit économique à réaliser.The object of the present invention is to propose a method for manufacturing a strip of thin sheet metal with improved stampability having a good ability both in expanding deformation and in shrinking deformation, as well as improved elongation at break. , and which is economical to produce.
La présente invention concerne plus particulièrement un procédé de fabrication d'une bande de tôle mince à emboutissabilité améliorée ayant une bonne aptitude à la déformation en expansion et à la déformation en rétreint, caractérisé en ce qu'il consiste à :
- élaborer un acier comprenant en millième de pour cent poids une teneur en carbone inférieure à 20, une teneur en silicium inférieure à 500, une teneur en manganèse inférieure à 1000, une teneur en phosphore inférieure à 100, une teneur en soufre inférieure à 50, une teneur en aluminium inférieure à 100, une teneur en azote inférieure à 10 et aucun, un ou plusieurs éléments parmi le titane, avec une teneur inférieure à 150, le niobium, avec une teneur inférieure à 150, le bore avec une teneur inférieure à 5, le reste étant du fer et des résiduels,
- réaliser un laminage à chaud.
- réaliser un laminage à froid avec un taux de réduction supérieur à 20%,
- réaliser un recuit à une température comprise entre la température de restauration de l'acier et 920°C,
- réaliser un second laminage à froid avec un taux de réduction supérieur à 20% en imprimant à la bande de tôle une rugosité déterminée,
- effectuer un second recuit à une température supérieure à la température de recristallisation de l'acier.
- develop a steel comprising in thousandths of a weight percent a carbon content of less than 20, a silicon content of less than 500, a manganese content of less than 1000, a phosphorus content of less than 100, a sulfur content of less than 50, an aluminum content of less than 100, a nitrogen content of less than 10 and none, one or more elements from titanium, with a content of less than 150, niobium, with a content of less than 150, boron with a content of less than 5, the remainder being iron and residuals,
- perform hot rolling.
- cold rolling with a reduction rate of more than 20%,
- anneal at a temperature between the steel restoration temperature and 920 ° C,
- perform a second cold rolling with a reduction rate of more than 20% by imparting a defined roughness to the sheet metal strip,
- perform a second annealing at a temperature higher than the recrystallization temperature of the steel.
Selon d'autres caractéristiques de l'invention :
- l'acier élaboré dans la première étape comprend en millième de pour cent poids une teneur en carbone comprise entre 2 et 20, une teneur en silicium comprise entre 100 et 500, une teneur en manganèse comprise entre 0 et 1000, en teneur en phosphore comprise entre 50 et 100, une teneur en soufre comprise entre 0 et 50, une teneur en aluminium comprise entre 0 et 100, une teneur en azote comprise entre 2 et 8, et un ou plusieurs éléments parmi le titane, avec une teneur comprise entre 0 et 150, le niobium, avec une teneur comprise entre 10 et 50, le bore, avec une teneur comprise entre 0 et 2, le reste étant du fer et des résiduels.
- le premier recuit est effectué à une température comprise entre la température de restauration de l'acier et sa température de recristallisation.
- le taux de réduction du premier laminage à froid est important et le taux de réduction du second laminage à froid est faible.
- le taux de réduction du premier laminage à froid est faible et le taux de réduction de second laminage à froid est important.
- le taux de réduction du premier laminage à froid est compris entre 35 et 50 % et le taux de réduction du second laminage à froid est compris entre 65 et 75 %.
- le taux de réduction du premier laminage à froid est compris entre 65 et 75 % et le taux de réduction du second laminage à froid est compris entre 35 et 50 %.
- Pendant le second laminage à froid, on imprime à la bande de tôle une rugosité moyenne Ra comprise entre 0,9 et 1,7 microns.
- the steel produced in the first stage comprises, in thousandths of a weight percent, a carbon content of between 2 and 20, a silicon content of between 100 and 500, a manganese content of between 0 and 1000, of phosphorus content between 50 and 100, a sulfur content between 0 and 50, an aluminum content between 0 and 100, a nitrogen content between 2 and 8, and one or more elements among titanium, with a content between 0 and 150, niobium, with a content of between 10 and 50, boron, with a content of between 0 and 2, the remainder being iron and residuals.
- the first annealing is carried out at a temperature between the temperature for restoring the steel and its recrystallization temperature.
- the reduction rate of the first cold rolling is high and the reduction rate of the second cold rolling is low.
- the reduction rate of the first cold rolling is low and the reduction rate of the second cold rolling is high.
- the reduction rate of the first cold rolling is between 35 and 50% and the reduction rate of the second cold rolling is between 65 and 75%.
- the reduction rate of the first cold rolling is between 65 and 75% and the reduction rate of the second cold rolling is between 35 and 50%.
- During the second cold rolling, the sheet strip is printed with an average roughness Ra of between 0.9 and 1.7 microns.
La présente invention concerne également une bande de tôle mince ayant une bonne aptitude à l'emboutissage obtenue par le procédé selon des caractéristiques ci-dessus.The present invention also relates to a strip of thin sheet metal having a good drawing ability obtained by the process according to the above characteristics.
Les caractéristiques et avantages apparaîtront au cours de la description qui va suivre, donnée uniquement à titre d'exemple.The characteristics and advantages will appear during the description which follows, given only by way of example.
L'invention concerne une bande de tôle mince en acier à emboutissabilité améliorée, c'est à dire présentant une limite d'élasticité faible, un coefficient de Lankford élevé supérieur à 2, de préférence 2,4 dans toutes les directions de la tôle, une consolidation importante, une ductilité importante et un module de Young élevé supérieur à 23.000 kg/mm2.The invention relates to a strip of thin sheet steel of improved stampability, that is to say having a low yield strength, a high Lankford coefficient greater than 2, preferably 2.4 in all directions of the sheet, significant consolidation, significant ductility and a high Young's modulus greater than 23,000 kg / mm 2 .
Pour obtenir une telle bande de tôle mince, on élabore dans un premier temps, de manière connue, par exemple au convertisseur d'aciérie, un acier dont la composition en millième de pour cent est la suivante :
De manière préférentielle, l'acier a la composition suivante, en millième de pour cent :
Compte-tenu de la teneur en carbone de cet acier, qui peut aller jusqu'à 20, il est envisageable de l'élaborer par soufflage argon moins coûteux que la technique du dégazage sous vide.Given the carbon content of this steel, which can range up to 20, it is possible to develop it by argon blowing, which is less costly than the vacuum degassing technique.
L'acier ainsi élaboré est ensuite coulé en brames puis laminé à chaud.The steel thus produced is then poured into slabs and then hot rolled.
La bande laminée à chaud est ensuite laminée à froid avec un taux de réduction supérieur à 20%.The hot rolled strip is then cold rolled with a reduction rate greater than 20%.
La bande ainsi laminée à froid est ensuite soumise à un recuit à une température comprise entre la température de restauration de l'acier et 920°C, de préférence entre la température de restauration de l'acier et sa température de recristallisation.The strip thus cold-rolled is then subjected to annealing at a temperature between the temperature for restoring the steel and 920 ° C., preferably between the temperature for restoring the steel and its recrystallization temperature.
Le recuit peut être indifféremment un recuit base ou un recuit continu.Annealing can either be basic annealing or continuous annealing.
On effectue ensuite un second laminage à froid avec un taux de réduction supérieur à 20% en imprimant à la bande de tôle une rugosité déterminée. Enfin, on effectue un second recuit à une température supérieure à la température de recristallisation de l'acier.A second cold rolling is then carried out with a reduction rate greater than 20% by imparting a determined roughness to the sheet metal strip. Finally, a second annealing is carried out at a temperature higher than the recrystallization temperature of the steel.
La Demanderesse a constaté qu'il est possible d'augmenter la valeur du coefficient de Lankford
Pour obtenir un module d'Young supérieur à 23.000 kg/mm2 et un coefficient de Lankford supérieur à 2, de préférence 2,4, il est nécessaire que, soit la réduction soit importante lors du second laminage à froid alors que la réduction était faible lors du premier laminage à froid, soit la réduction soit faible lors du premier laminage à froid alors que la réduction était importante lors du premier laminage à froid.To obtain a Young's modulus greater than 23,000 kg / mm 2 and a Lankford coefficient greater than 2, preferably 2.4, it is necessary that either the reduction is significant during the second cold rolling while the reduction was low during the first cold rolling, either the reduction or small during the first cold rolling while the reduction was significant during the first cold rolling.
Deux cas de figure peuvent donc être envisagés.Two cases can therefore be envisaged.
Le premier cas de figure, dans lequel le taux de réduction du premier laminage à froid est faible, tout en étant supérieur à 20%, de préférence de l'ordre de 35 à 50 %, et le taux de réduction du second laminage est important, de préférence de l'ordre de 65 à 75 %.The first scenario, in which the reduction rate of the first cold rolling is low, while being greater than 20%, preferably of the order of 35 to 50%, and the reduction rate of the second rolling is high , preferably of the order of 65 to 75%.
Le second cas de figure, dans lequel le taux de réduction du premier laminage à froid est important, de préférence de l'ordre de 65 à 75 % et le taux de réduction du second laminage à froid est faible, tout en étant supérieur à 20%, de préférence de l'ordre de 35 à 50 %.The second scenario, in which the reduction rate of the first cold rolling is high, preferably of the order of 65 to 75% and the reduction rate of the second cold rolling is low, while being greater than 20 %, preferably of the order of 35 to 50%.
Pour obtenir les qualités d'emboutissabilité requises, il est également intéressant pendant le second laminage à froid de la tôle, d'imprimer sur celle-ci au moyen des cylindres de laminage une rugosité requise.To obtain the required stamping qualities, it is also advantageous during the second cold rolling of the sheet, to print on it by means of the rolling rolls a required roughness.
A titre d'exemple, la rugosité imprimée est telle que la rugosité moyenne Ra est comprise entre 0,9 et 1,7 microns.For example, the printed roughness is such that the average roughness Ra is between 0.9 and 1.7 microns.
De préférence, la rugosité moyenne Ra est comprise entre 1,2 et 1,7 pour favoriser l'emboutissage. Mais si on désire obtenir un aspect plus brillant à la tôle, tout en conservant une bonne emboutissabilité, on imprime à la tôle une rugosité moyenne Ra comprise entre 0,9 et 1,4 microns.Preferably, the average roughness Ra is between 1.2 and 1.7 to promote stamping. But if one wishes to obtain a more shiny appearance to the sheet, while retaining good stampability, the sheet is printed with an average roughness Ra of between 0.9 and 1.4 microns.
Cette opération permet en supprimant l'opération de skin-pass de garantir un coefficient de Lankford élevé supérieur à 2, de préférence 2,4 et une limite d'élasticité faible car l'opération de skin-pass a pour conséquence d'augmenter la limite d'élasticité du métal, et de dégrader le coefficient d'écrouissage
Plusieurs essais ont été réalisés avec plusieurs types d'acier dont les compositions sont les suivantes en millième de pour cent, le complément étant du fer :
Comme on peut le constater, les aciers A et B sont des aciers conformes à l'invention et l'acier C correspond à une composition selon l'état de la technique.As can be seen, steels A and B are steels according to the invention and steel C corresponds to a composition according to the state of the art.
La température de restauration de l'acier A, qui a été élaboré avec un premier recuit base, est égale à 450°C et sa température de recristallisation est égale à 680°C.The restoration temperature of steel A, which was produced with a first base annealing, is equal to 450 ° C. and its recrystallization temperature is equal to 680 ° C.
La température de restauration de l'acier B, qui a été élaboré avec un premier recuit continu, est égale à 450°C et sa température de recristallisation est égale à 630°C.The restoration temperature of steel B, which was produced with a first continuous annealing, is equal to 450 ° C. and its recrystallization temperature is equal to 630 ° C.
Chacun des trois types d'acier a ensuite subi des traitements de laminage et de recuit différents et on a ainsi réalisé plusieurs bandes de tôle d'épaisseur inférieure à 1 mm.Each of the three types of steel was then subjected to different rolling and annealing treatments and several sheet metal strips less than 1 mm thick were thus produced.
Dans chaque tôle, on a prélevé une série d'éprouvettes et réalisé les divers essais pour déterminer les paramètres caractéristiques de cet acier.
Comme on le voit dans ce tableau, l'acier de l'invention permet d'obtenir par rapport à l'acier C de l'état de la technique, un gain significatif en terme de ductilité et en terme d'emboutissabilité.As can be seen in this table, the steel of the invention makes it possible to obtain, compared with steel C of the prior art, a significant gain in terms of ductility and in terms of drawability.
L'avantage d'imprimer une rugosité contrôlée pendant le second laminage à froid permet d'obtenir une limite d'élasticité Re sensiblement plus faible que si on s'abstenait d'imprimer cette rugosité.The advantage of printing a controlled roughness during the second cold rolling makes it possible to obtain an elastic limit Re appreciably lower than if one abstained from printing this roughness.
Claims (9)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9508643A FR2736933B1 (en) | 1995-07-18 | 1995-07-18 | METHOD FOR MANUFACTURING A THIN SHEET STRIP WITH IMPROVED DRAWING |
FR9508643 | 1995-07-18 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0754770A1 true EP0754770A1 (en) | 1997-01-22 |
EP0754770B1 EP0754770B1 (en) | 2001-11-14 |
Family
ID=9481066
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP96401347A Expired - Lifetime EP0754770B1 (en) | 1995-07-18 | 1996-06-20 | Method of producing a thin steel strip having improved deep-drawing properties |
Country Status (9)
Country | Link |
---|---|
EP (1) | EP0754770B1 (en) |
JP (1) | JPH0931539A (en) |
KR (1) | KR970005422A (en) |
AT (1) | ATE208831T1 (en) |
DE (1) | DE69616887T2 (en) |
DK (1) | DK0754770T3 (en) |
ES (1) | ES2164222T3 (en) |
FR (1) | FR2736933B1 (en) |
PT (1) | PT754770E (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0896069A1 (en) * | 1997-08-07 | 1999-02-10 | Sollac | Method of making thin ultra-low-carbon steel strip for manufacturing deep-drawn products for packages and thin strips obtained thereby |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1045641A (en) * | 1964-04-25 | 1966-10-12 | Opel Adam Ag | Steel sheet or strip |
GB2028690A (en) * | 1978-08-22 | 1980-03-12 | Kawasaki Steel Co | Steel sheets |
JPS61291924A (en) * | 1985-06-17 | 1986-12-22 | Nippon Steel Corp | Manufacture of steel sheet for press forming superior in workability |
EP0231864A2 (en) * | 1986-02-06 | 1987-08-12 | Hoesch Stahl Aktiengesellschaft | Non-ageing steel strip |
EP0417699A2 (en) * | 1989-09-11 | 1991-03-20 | Kawasaki Steel Corporation | Cold-rolled steel sheet for deep drawing and method of producing the same |
EP0484960A2 (en) * | 1990-11-09 | 1992-05-13 | Nippon Steel Corporation | Cold-rolled steel strip having excellent combined press formability and method of producing same |
-
1995
- 1995-07-18 FR FR9508643A patent/FR2736933B1/en not_active Expired - Fee Related
-
1996
- 1996-06-20 ES ES96401347T patent/ES2164222T3/en not_active Expired - Lifetime
- 1996-06-20 AT AT96401347T patent/ATE208831T1/en not_active IP Right Cessation
- 1996-06-20 PT PT96401347T patent/PT754770E/en unknown
- 1996-06-20 DK DK96401347T patent/DK0754770T3/en active
- 1996-06-20 DE DE69616887T patent/DE69616887T2/en not_active Expired - Fee Related
- 1996-06-20 EP EP96401347A patent/EP0754770B1/en not_active Expired - Lifetime
- 1996-07-16 KR KR1019960028752A patent/KR970005422A/en not_active Application Discontinuation
- 1996-07-17 JP JP8206564A patent/JPH0931539A/en not_active Withdrawn
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB1045641A (en) * | 1964-04-25 | 1966-10-12 | Opel Adam Ag | Steel sheet or strip |
GB2028690A (en) * | 1978-08-22 | 1980-03-12 | Kawasaki Steel Co | Steel sheets |
JPS61291924A (en) * | 1985-06-17 | 1986-12-22 | Nippon Steel Corp | Manufacture of steel sheet for press forming superior in workability |
EP0231864A2 (en) * | 1986-02-06 | 1987-08-12 | Hoesch Stahl Aktiengesellschaft | Non-ageing steel strip |
EP0417699A2 (en) * | 1989-09-11 | 1991-03-20 | Kawasaki Steel Corporation | Cold-rolled steel sheet for deep drawing and method of producing the same |
EP0484960A2 (en) * | 1990-11-09 | 1992-05-13 | Nippon Steel Corporation | Cold-rolled steel strip having excellent combined press formability and method of producing same |
Non-Patent Citations (2)
Title |
---|
FEKETE J R ET AL: "ADVANCED SHEET STEELS FOR AUTOMOTIVE APPLICATIONS", JOM, vol. 44, no. 1, 1 January 1992 (1992-01-01), pages 17 - 21, XP000262949 * |
PATENT ABSTRACTS OF JAPAN vol. 011, no. 163 (C - 424) 26 May 1987 (1987-05-26) * |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0896069A1 (en) * | 1997-08-07 | 1999-02-10 | Sollac | Method of making thin ultra-low-carbon steel strip for manufacturing deep-drawn products for packages and thin strips obtained thereby |
FR2767078A1 (en) * | 1997-08-07 | 1999-02-12 | Lorraine Laminage | PROCESS FOR THE PREPARATION OF A THIN SHEET IN ULTRA LOW CARBON STEEL FOR THE PRODUCTION OF STAMPED PRODUCTS FOR PACKAGING AND THIN SHEET OBTAINED |
US6767415B1 (en) | 1997-08-07 | 2004-07-27 | Sollac | Process for producing a thin sheet of ultra-low-carbon steel for the manufacture of drawn products for packaging and thin sheet obtained |
Also Published As
Publication number | Publication date |
---|---|
ES2164222T3 (en) | 2002-02-16 |
PT754770E (en) | 2002-05-31 |
JPH0931539A (en) | 1997-02-04 |
DK0754770T3 (en) | 2002-02-25 |
FR2736933B1 (en) | 1997-08-22 |
EP0754770B1 (en) | 2001-11-14 |
DE69616887T2 (en) | 2002-05-29 |
ATE208831T1 (en) | 2001-11-15 |
KR970005422A (en) | 1997-02-19 |
FR2736933A1 (en) | 1997-01-24 |
DE69616887D1 (en) | 2001-12-20 |
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