EP2534271B1 - Feuille d'acier appropriée pour un émaillage et procédé de fabrication d'une telle feuille - Google Patents

Feuille d'acier appropriée pour un émaillage et procédé de fabrication d'une telle feuille Download PDF

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Publication number
EP2534271B1
EP2534271B1 EP11713766.1A EP11713766A EP2534271B1 EP 2534271 B1 EP2534271 B1 EP 2534271B1 EP 11713766 A EP11713766 A EP 11713766A EP 2534271 B1 EP2534271 B1 EP 2534271B1
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Prior art keywords
steel sheet
level
bulk
sheet
enamelling
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EP11713766.1A
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German (de)
English (en)
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EP2534271A1 (fr
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Nele Van Steenberge
Marc Leveaux
Lode Duprez
Philippe Gousselot
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ArcelorMittal SA
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ArcelorMittal Investigacion y Desarrollo SL
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Priority to PL11713766T priority Critical patent/PL2534271T3/pl
Priority to SI201130570T priority patent/SI2534271T1/sl
Priority to RS20150565A priority patent/RS54209B1/en
Publication of EP2534271A1 publication Critical patent/EP2534271A1/fr
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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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper

Definitions

  • the present invention is related to a steel sheet suitable for enamelling, and to a method for the superficial decarburization of a steel sheet, as a preparation for enamelling the steel.
  • the carbon level of a steel sheet has an important influence on the results in terms of surface quality of an enamel layer applied on the surface of the sheet.
  • a high carbon level at the steel surface may give rise to CO-gas bubble formation, which shows up as black spots and craters in the enamel surface.
  • this carbon forms coarse cementite during hot rolling which cracks upon cold rolling. These cracks are capable of capturing hydrogen which enters the steel during the enamelling process. When hydrogen is insufficiently captured, pressure will rise at the steel/enamel surface which gives rise to the so-called 'fish-scale' deformation of the enamel.
  • Document JP-A-2282421 describes such a method, wherein a continuously cast and annealed non-aging steel sheet for enamelling is produced, characterized in that a continuous-cast steel slab containing C between 0.0025 and 0.0050wt%, Si max. 0.03wt%, Mn between 0.1 and 0.6wt%, P between 0.005 and 0.03wt%, S between 0.005 and 0.03wt%, Al max. 0.01wt%, N max.
  • JP-A-6116634 describes a similar method, but wherein the starting material has no vanadium and the initial C level is up to 0.015wt% and B is added instead of V for H-trapping.
  • the prior art decarburized sheets have rather low formability as testified by the values of the Lankford coefficient (r m ). These values do not exceed 1.8 which is a concern when deep-drawing is foreseen.
  • figure 1 of JP6116634 shows that r m values between 1.6 and 1.8 are only achieved for a very narrow range of carbon level before decarburizing annealing. Below 0.0050wt%C and above 0.0150wt%C, the r m value is deteriorated.
  • the present invention aims to provide a partially decarburized steel sheet suitable for enamelling which do not suffer from the drawbacks of the above cited prior art.
  • the invention is related to steel sheets and products and to a production method as disclosed in the appended claims.
  • the invention is thus related to a rolled steel sheet suitable for enamelling, said sheet having a carbon profile, defined by a gradient in the C-level from a level C surface at at least one surface of the sheet, to a level C bulk in the bulk of the sheet, C bulk being higher than C surface , and with :
  • the steel sheet of the invention has an r m value between 1.8 and 2.1.
  • C surface is between 0.005wt% and 0.015wt%, or between 0 and 0.005wt%.
  • C bulk is between 0.02wt% and 0.08wt%, or between 0.025wt% and 0.08wt% or between 0.025wt% and 0.06wt%.
  • the Al-level is between 0.02wt% and 0.06wt%.
  • said depth is between 130 ⁇ m and 200 ⁇ m.
  • the invention is equally related to an enamelled steel sheet consisting of a steel sheet according to any of the above paragraphs, provided with an enamel layer.
  • the invention is further related to a steel product produced from a sheet according to the invention, and to an enamelled steel product consisting of a such a product, provided with an enamel layer.
  • the invention is also related to a method for producing a rolled steel sheet for enamelling, comprising the steps of :
  • said continuous annealing takes place at an anneal temperature between 760°C and 850°C, and during a decarburizing time between 45s and 300s.
  • the anneal temperature is between 800°C and 850°C.
  • the initial C-level is between 0.025wt% and 0.08wt% or between 0.025wt% and 0.06wt%.
  • the initial Al-level is between 0.02wt% and 0.06wt%.
  • the ratio pH 2 O/pH 2 is between 0.04 and 0.25.
  • the method of the invention may further comprise an over-ageing step at a temperature between 350°C and 450°C during a timespan between 100s and 500s.
  • the method may further comprise a skinpass step with a reduction of between 0.3% and 1.5%.
  • the steel sheet of the invention has a C-profile, defined by a gradient in the C-level from a lower value C surface at the surface to a higher value C bulk in the bulk.
  • the sheet is obtainable by a method which includes a continuous decarburization step, as will be described further in this text.
  • Figure 1 illustrates the carbon-distribution across the thickness of two sheets according to the invention, with a thickness of 0.7mm.
  • Curve 10 illustrates a sheet which comprises a bulk portion 11, where the C-level C bulk is substantially constant, and two surface portions 12 (one on each side of the sheet), each surface portion exhibiting the C-profile.
  • the surface level is defined as the minimum value of the C-profile, measured by a suitable measurement technique (e.g.
  • GD-OES Glow Discharge Optical Emission Spectroscopy
  • the C-level at the surface is maximum 0.015wt%, whereas C bulk is higher than zero and lower than or equal to 0.08wt%.
  • C bulk is higher than C surface .
  • C surface is between 0.005wt% and 0.015wt%.
  • C surface is between 0 and 0.005wt%.
  • Curve 10 is an example of a sheet where the decarburization has not taken place over the entire thickness of the sheet.
  • the level C bulk is equal to the initial C-level applied in the production method (described further in more detail).
  • C bulk is then between 0.02wt% and 0.08wt%, or between 0.025wt% and 0.08wt, or between 0.025wt% and 0.06wt% or between 0.025wt% and 0.05wt%.
  • Curve 13 illustrates the case where decarburization has continued until the middle plane of the sheet. In this case, C bulk is smaller than the initial C-level of the method, and the C-profile extends over each half-width of the sheet.
  • the decarburized sheet according to the invention further comprises Al, Mn and possibly S, Cu and Ca. Contrary to the prior art references, the oxygen level is to be kept lower than 0.01wt%. According to a preferred embodiment of the steel sheet of the invention, oxygen is not added deliberately to the composition, but is allowed only at impurity levels. Fish scaling resistance is ensured by the higher initial C-level, so no oxide formation is required for this purpose. This means that no special alloying elements such as V are included. Also, N is kept as low as possible.
  • the Al-level in the sheet of the invention is between 0.012wt% and 0.07wt%, which is higher than the allowed Al-level in the prior art references cited above.
  • Al needs to be limited to avoid deoxidation, so as to ensure the formation of the oxides that will work against fish-scaling.
  • Al is mandatory for deoxidation and binding of free N to avoid the ageing of the mechanical properties.
  • Adding Al at levels higher than 0.07wt% means an increase in cost of the process, and a deterioration of the enamelling quality.
  • a more preferred range for the Al-level, related to more optimized conditions in terms of deoxidation and cost/enamelling quality is between 0.02wt% and 0.06wt%.
  • Mn is present between 0.12wt% and 0.45wt%. This element is added to control the strength properties of the steel and to avoid the formation of free sulphur.
  • Copper, Sulphur and Calcium may optionally be added above the impurity level, more precisely in the ranges 0.025wt% to 0.1wt%, 0.008wt% to 0.04wt% and 0.0005wt% to 0.005wt% respectively. These elements improve the enamelling quality.
  • the balance of the composition of the steel sheet according to the invention consists of Fe and incidental impurities.
  • the following elements may be present as impurities at levels which are preferably lower than the values (in wt%) given in table 1 :
  • Table 1 impurity levels Si ⁇ 0.1 P ⁇ 0.03 Ti ⁇ 0.01 Cr ⁇ 0.2 Ni ⁇ 0.2 As ⁇ 0.02 Sn ⁇ 0.02 Nb ⁇ 0.01 V ⁇ 0.01 Sb ⁇ 0.02 Mo ⁇ 0.03 B ⁇ 0.0005 N ⁇ 0.007
  • the depth of the C-profile being defined as the depth where the C-level reaches (C bulk + C surfare ) /2, is higher than 75 ⁇ m, to ensure good enamelling capability. According to an embodiment, said depth is between 130 ⁇ m and 200 ⁇ m.
  • Steel sheets according to the invention i.e. with a C-level at the surface between 0 and 0.015wt% are suitable for 2C/1F enamelling, i.e. enamelling by applying a ground coat enamel, followed by an outer enamel coating, both coatings being subjected to one firing step, and for 1C/1F enamelling, i.e. enamelling by applying one enamel layer subjected to one firing step.
  • Steel sheets with low C-levels (i.e. 0.005wt% and less) at the surface may be suitable also for Direct White Enamelling (DWE).
  • DWE Direct White Enamelling
  • the r m value of a steel sheet according to the invention is between 1.8 and 2.1. This means that the steel sheet has better formability than the prior art steel sheets referred to above.
  • the 'r' value refers to the plastic strain ratio (also known as the anisotropy factor), being the ratio of the true strain in the width direction to the true strain in the thickness direction when a sheet material is pulled in uniaxial tension beyond its elastic limit.
  • the 'r m ' value is defined as 1 ⁇ 4 (r 90 + 2*r 45 + r 0 ), with r 90 , r 45 and r 0 the r-values as defined above, measured on samples oriented respectively at 90°, 45° and 0° with respect to the rolling direction.
  • fish scaling resistance is ensured by the higher initial C-level applied in the method (see further).
  • the steel sheet of the invention can be produced by subjecting a steel slab with a specific initial steel composition to hot rolling, coiling and cold rolling, and by subjecting the cold-rolled sheet to continuous superficial decarburization.
  • the initial composition is mainly characterized by a higher C-level compared to the prior art, and by a higher Al-level and a lower oxygen level. No deliberate addition of elements like V, Nb or B is done, while still allowing to produce enamelled steel sheets with a high fish scale resistance and good enamel surface quality.
  • the initial C-level is between 0.02wt% and 0.08wt%, more preferably between 0.025wt% and 0.08wt%. This is higher than the initial C-levels disclosed in the prior art references referred to above.
  • the method of the invention allows to obtain steel sheets with improved formability characteristics compared to the prior art.
  • JP6116634 indicates that above 0.015wt% of initial carbon, it is not possible to obtain acceptable decarburization and good formability, the starting composition of the invention does not encounter these problems. Decarburization is possible down to an acceptable level, while formability is excellent.
  • the initial C-level is lower than 0.02wt%, insufficient cementite formation occurs which deteriorates fish scale resistance.
  • C-levels above 0.08wt% lead to too high strength levels and thus reduced formability.
  • Specific ranges for the initial C-level, related to more optimized characteristics in terms of fish scale resistance and strength/formability are between 0.025wt% and 0.06wt% and between 0.025wt% and 0.05wt%.
  • the initial steel composition according to the method of the invention further comprises Al, Mn and possibly O, S, Cu and Ca in the same ranges as the decarburized sheet described above, the balance being Fe and the incidental impurities listed in Table 1.
  • a more preferred range for the initial Al-level, related to more optimized conditions in terms of deoxidation and cost/enamelling quality is between 0.02wt% and 0.06wt%.
  • oxygen is not added deliberately to the composition, but is allowed only at impurity levels.
  • the method of the invention comprises standard steps of hot rolling and cold rolling a steel slab of the above composition.
  • the slab is (re)heated at a temperature above 1050°C, subjected to hot rolling with a finishing temperature between 850°C and 950°C, and coiling at coiling temperature between 620°C and 770°C.
  • cold rolling is performed with a reduction of minimum 50%.
  • the final thickness of the cold rolled sheet is preferably between 0.2 and 2mm.
  • the decarburization anneal is done in an annealing furnace for continuous annealing (i.e. annealing while the cold-rolled sheet moves through the furnace at a given speed, said speed determining the anneal time, i.e. the time spent at the annealing temperature) as known in the art, possibly provided with a vapour injection device for applying a given annealing atmosphere.
  • Figure 2 shows an example of a lay-out of an annealing furnace usable in the method of the invention, starting with heating phase 1 wherein the temperature rises to the annealing temperature.
  • Phase 2 represents the actual annealing (soaking) phase.
  • Phase 3 is an overageing step.
  • Phase 2 can consist of one or more periods with a different (constant or average) annealing temperature and a different annealing atmosphere in each period. Practically speaking, the different periods at different conditions can be obtained by dividing the annealing zone in subsections and by injecting H 2 O vapour into an atmosphere comprising H 2 , at various points along the annealing line (see example further in this description).
  • the superficial decarburization is done under a decarburizing atmosphere comprising water vapour and hydrogen gas, the remainder being essentially nitrogen gas, with the H 2 content between 1vol% and 95vol%, the H 2 O content between 0.04vol% and 33vol%, the ratio of partial pressures pH 2 O/pH 2 being between 0.04 and 0.5, more preferably between 0.04 and 0.25.
  • the above composition describes the atmosphere at the start of the decarburizing time. It is clear that during decarburization, the atmosphere composition will change, primarily due to the decarburization reaction taking place (formation of H 2 and CO). Also at the start of the decarburizing time, small amounts of other gases may already have formed or may be present as impurities in the atmosphere.
  • the total pressure under which the superficial decarburization anneal takes place may be atmospheric pressure, or a pressure different from atmospheric but within generally known boundaries applied in this type of annealing process.
  • the decarburizing atmosphere can be prepared with a mixture of H 2 and N 2 with between 1,5 and 5% H 2 in which H 2 O vapour is injected so that pH 2 O/pH 2 is between 0.04 and 0.5.
  • the minimum value of this ratio ensures that sufficient H 2 O is present to obtain decarburization according to the formula C + H 2 O ⁇ CO + H 2 .
  • the maximum of said range ensures that oxidation of Fe and of the furnace is avoided.
  • a more preferred range for pH 2 O/pH 2 related to more optimized conditions in terms of sufficient decarburization and avoiding the occurrence of Fe-oxidation is between 0.04 and 0.25.
  • the decarburizing atmosphere is applied during at least one of said periods with a different (constant or average) annealing temperature and a different annealing atmosphere in each period, preferably during the totality of phase 2.
  • the "decarburizing time' refers to the time spent under the conditions of the decarburizing atmosphere.
  • the decarburizing time and the anneal temperature are chosen so as to obtain a steel sheet according to the invention. It is within the skilled person's knowledge to find suitable combinations of decarburizing time and anneal temperature based on the examples given further in this description. According to a preferred embodiment, the decarburizing time is between 45s and 300s and the anneal temperature between 760°C and 850°C. When the ratio pH 2 O/pH 2 is lower than about 0.1, the decarburizing time is preferably higher than 70s. A more preferred range of the anneal temperature, applicable in combination with any decarburizing time between 45s and 300s is between 800°C and 850°C. The temperature is not necessarily constant during the decarburizing time.
  • Fluctuations of the temperature may occur due to variations in the line speed for example.
  • An over-ageing step may be applied at a temperature between 350°C and 450°C during a timespan between 100s and 500s.
  • a skinpass may further be applied with a reduction of between 0.3% and 1.5%.
  • results from industrial trials performed by the applicant will be described hereafter, as well as a number of laboratory trials. All tested samples were produced from starting compositions according to the invention.
  • the coiling temperature was 725°C.
  • Two industrial trials were conducted.
  • the thickness of the cold rolled sheet subjected to decarburization annealing in industrial trial 1 was 0.6mm; in the second industrial trial the thickness was 1mm.
  • the continuous annealing line in which the industrial trials were conducted consists of a heating section, two soaking areas, a cooling and an overaging part.
  • the annealing atmosphere consisted mainly of a mixture of H 2 and N 2 , with H 2 O vapour being injected in the first and/or the second soaking area.
  • H 2 O vapour was injected only in the second soaking area.
  • H 2 O was injected in the first and the second soaking area.
  • Overageing was performed in both trials at 400°C.
  • the overageing time depended on the line speed, e.g. at 180m/min line speed, the overageing time was 232s.
  • Table 2 shows the annealing conditions for both trials (numbered trial 1 and trial 2).
  • Table 3 shows the composition besides C, for a number of the samples shown in table 1.
  • phase 2 as shown in figure 1 comprises a first period wherein the conditions of the present invention are not met, and a second period wherein these conditions are met. Such a process falls within the scope of the present invention.
  • H 2 O-injection was performed in both soaking areas.
  • the decarburizing time indicated here is the time spent in soaking areas 1 and 2.
  • the anneal temperature is the average of the temperatures in soaking areas 1 and 2.
  • the pH 2 O/pH 2 values indicated in table 1 are the average values in soaking area 1 in which more H 2 O was injected.
  • the pH 2 O/pH 2 in soaking area 2 is estimated to be also within the range of 0.04-0.5.
  • longer decarburizing times could be achieved as compared to the first trial, for similar line velocities, leading to stronger decarburization.
  • Table 2 summarizes the results after decarburization in terms of the C-level at the surface (i.e. minimum level of the C-profile, measured by GD-OES), the depth of the C-profile, and the quality of an enamel layer produced on the surface of the samples.
  • Samples 25 to 35 yielded a bad enamelling aspect, which can be ascribed to either an insufficient depth of the C-profile (as determined by the depth where the C-level reaches (C surface +C bulk /2), and/or a C level at the surface which is too high.
  • the reason for these negative results can be ascribed to the test conditions, either the anneal temperature which is too low, the decarburizing time too short, or the pH 2 O/pH 2 ratio too low, or a combination of these factors.
  • Table 4 shows the mechanical properties of a number of samples taken from the sheets of the industrial trials 1 and 2. Importantly, the formability in terms of the r m value is excellent, despite the initial C-level which is higher than in the prior art : r m is between 1.8 and 2.1. These results prove that the method of the invention allows to produce steel sheets suitable for enamelling, starting from an initial C-level higher than 0.02wt%, the resulting sheets allowing good enamelling quality and fish scale resistance, and having very good formability characteristics.
  • Table 2 Overview of experimental conditions and results sample n° Trial nr initial Cl (ppm 1 ) decarburizing time (s) anneal temp.
  • the depth-values given in table 1 are values of the depth where the C-level reaches (C surface +C bulk ) /2.
  • the depth measurements indicated with ⁇ *' show the maximum depth which could be measured with the applied equipment. The real value is thus higher than this value.
  • Table 3 composition of samples (C-level in table 1, remaining elements are beneath impurity level, the remainder is Fe) Sample n° Al(wt%) Mn(wt%) Cu (wt%) S (wt%) 1 0.024 0.18 0.022 0.0049 5 0.03 0.18 0.028 0.0046 6 0.028 0.19 0.041 0.0052 9 0.035 0.18 0.029 0.0088 11 0.034 0.17 0.028 0.0077
  • Table 4 mechanical properties sample n° initial C-level (ppm) Anneal Temp (°C) Anneal time (s) pH2O/pH2 (-) Rp0.2 (MPa) Rm (MPa) r_m Thickness (mm) 23 490 796 209 0,09 189 318 1,8 0.6 1 362 807 126 0,12 182 318 1,9 0,6 5 367 782 105 0,16 189 319 1,8 0.6 19 391 821 105 0.08 185 320 1,8 1 15 375 824 45 0,09 187 3

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  • Engineering & Computer Science (AREA)
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Claims (19)

  1. Feuille d'acier laminée appropriée pour un émaillage, ladite feuille présentant un profil de carbone, défini par un gradient du niveau de C d'un niveau Csurface au niveau d'au moins une surface de la feuille, à un niveau Cmasse dans la masse de la feuille, Cmasse étant supérieur à Csurface, et avec :
    - Cmasse supérieur à 0 et inférieur ou égal à 0,08 % en poids,
    - Csurface entre 0 et 0,015 % en poids,
    - Al entre 0,012 % en poids et 0,07 % en poids,
    - Mn entre 0,12 % en poids et 0,45 % en poids,
    - O inférieur à 0,01 % en poids
    et optionnellement :
    - Cu entre 0,025 % en poids et 0,1 % en poids,
    - S entre 0,008 % en poids et 0,04 % en poids,
    - Ca entre 0,0005 % en poids et 0,005 % en poids,
    le reste étant du Fe et des impuretés accidentelles, dans laquelle lesdites impuretés peuvent comprendre (en % en poids) : Si < 0,1, P < 0,03, Ti < 0,01, Cr < 0,2, Ni < 0,2, As < 0,02, Sn < 0,02, Nb < 0,01, V < 0,01, Sb < 0,02, Mo < 0,03, B < 0,0005, N < 0,007,
    et dans laquelle la profondeur à laquelle le niveau de C atteint (Cmasse + Csurface)/2, est supérieure à 75 µm.
  2. Feuille d'acier selon la revendication 1, ayant une valeur rm entre 1,8 et 2,1.
  3. Feuille d'acier selon la revendication 1 ou 2, dans laquelle Csurface est entre 0, 005 % en poids et 0,015 % en poids.
  4. Feuille d'acier selon la revendication 1 ou 2, dans laquelle Csurface est entre 0 et 0, 005 % en poids.
  5. Feuille d'acier selon l'une quelconque des revendications 1 à 4, dans laquelle Cmasse est entre 0,02 % en poids et 0,08 % en poids.
  6. Feuille d'acier selon la revendication 5, dans laquelle Cmasse est entre 0,025 % en poids et 0,08 % en poids.
  7. Feuille d'acier selon la revendication 5, dans laquelle Cmasse est entre 0,025 % en poids et 0,06 % en poids.
  8. Feuille d'acier selon l'une quelconque des revendications 1 à 7, dans laquelle le niveau d'Al est entre 0,02 % en poids et 0,06 % en poids.
  9. Feuille d'acier selon l'une quelconque des revendications 1 à 8, dans laquelle ladite profondeur est entre 130 µm et 200 µm.
  10. Feuille d'acier émaillée constituée d'une feuille d'acier selon l'une quelconque des revendications 1 à 9 présentant une couche d'émail.
  11. Procédé de production d'une feuille d'acier laminée pour émaillage, comprenant les étapes consistant à :
    - soumettre une brame d'acier à un laminage à chaud suivi d'un bobinage et d'un laminage à froid, de manière à obtenir une feuille d'acier laminée à froid, ladite brame comprenant la composition initiale suivante :
    - C entre 0,02 % en poids et 0,08 % en poids,
    - Al entre 0,012 % en poids et 0,07 % en poids,
    - Mn entre 0,12 % en poids et 0,45 % en poids,
    - O inférieur à 0,01 % en poids
    et optionnellement :
    - Cu entre 0,025 % en poids et 0,1 % en poids,
    - S entre 0,008 % en poids et 0,04 % en poids,
    - Ca entre 0,0005 % en poids et 0,005 % en poids,
    - le reste étant du Fe et des impuretés accidentelles, dans lequel lesdites impuretés peuvent comprendre (en % en poids) : Si < 0,1, P < 0,03, Ti < 0,01, Cr < 0,2, Ni < 0,2, As < 0,02, Sn < 0,02, Nb < 0,01, V < 0,01, Sb < 0,02, Mo < 0,03, B < 0,0005, N < 0,007,
    - soumettre ladite feuille laminée à froid à une étape de recuit continu, dans lequel ladite feuille est exposée pendant une durée de décarburation à une atmosphère décarburante comprenant de la vapeur d'eau et un gaz d'hydrogène, dans lequel la teneur en H2 est entre 1 % en vol et 95 % en vol, la teneur en H2O entre 0,04 % en vol et 33 % en vol, le reste étant principalement du gaz d'azote, le rapport pH2O/pH2 étant entre 0,04 et 0,5.
  12. Procédé selon la revendication 11, dans lequel ledit recuit continu a lieu à une température de recuit entre 760 °C et 850 °C, et pendant une durée de décarburation entre 45 s et 300 s.
  13. Procédé selon la revendication 12, dans lequel la température de recuit est entre 800 °C et 850 °C.
  14. Procédé selon l'une quelconque des revendications 13 à 15, dans lequel le niveau de C initial est entre 0, 025 % en poids et 0,08 % en poids.
  15. Procédé selon la revendication 14, dans lequel le niveau de C initial est entre 0,025 % en poids et 0,06 % en poids.
  16. Procédé selon l'une quelconque des revendications 11 à 15, dans lequel le niveau d'Al initial est entre 0,02 % en poids et 0,06 % en poids.
  17. Procédé selon l'une quelconque des revendications 11 à 16, dans lequel le rapport pH2O/pH2 est entre 0,04 et 0,25.
  18. Procédé selon l'une quelconque des revendications 11 à 17, comprenant en outre une étape de survieillissement à une température entre 350 °C et 450 °C pendant un laps de temps entre 100 s et 500 s.
  19. Procédé selon la revendication 18, comprenant en outre une étape d'écrouissage avec une réduction située entre 0,3 % et 1,5 %.
EP11713766.1A 2011-04-08 2011-04-08 Feuille d'acier appropriée pour un émaillage et procédé de fabrication d'une telle feuille Active EP2534271B1 (fr)

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PL11713766T PL2534271T3 (pl) 2011-04-08 2011-04-08 Blacha stalowa odpowiednia do emaliowania i sposób wytwarzania takiej blachy
SI201130570T SI2534271T1 (sl) 2011-04-08 2011-04-08 Za emajliranje primerna jeklena pločevina ter postopek izdelave tovrstne pločevine
RS20150565A RS54209B1 (en) 2011-04-08 2011-04-08 STEEL SHEET SUITABLE FOR ENAMELING AND PROCEDURE FOR MANUFACTURING SUCH SHEET

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PCT/EP2011/055477 WO2012136270A1 (fr) 2011-04-08 2011-04-08 Feuille d'acier appropriée pour un émaillage et procédé de fabrication d'une telle feuille

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US11236427B2 (en) 2017-12-06 2022-02-01 Polyvision Corporation Systems and methods for in-line thermal flattening and enameling of steel sheets
JP6806128B2 (ja) * 2018-01-09 2021-01-06 Ｊｆｅスチール株式会社 冷延鋼板の判定方法および冷延鋼板の製造方法
KR102305878B1 (ko) * 2019-12-20 2021-09-27 주식회사 포스코 법랑용 강판 및 그 제조방법
KR102405223B1 (ko) * 2020-11-05 2022-06-02 주식회사 포스코 법랑용 강판 및 그 제조방법
KR102469876B1 (ko) * 2020-12-18 2022-11-23 주식회사 포스코 밀착성이 우수한 고강도 법랑용 냉연강판 및 이의 제조방법
CN113913699A (zh) * 2021-10-26 2022-01-11 攀钢集团攀枝花钢铁研究院有限公司 屈服强度300MPa级的冷轧搪瓷钢生产方法

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US3598658A (en) * 1967-05-20 1971-08-10 Yawata Iron & Steel Co Method for manufacturing cold-rolled steel sheet
EP0228242A3 (fr) * 1985-12-23 1989-03-22 Tektronix, Inc. Analyseur non-intrusif de performance de microprocesseur
JPH02282421A (ja) 1989-04-24 1990-11-20 Nippon Steel Corp 連続鋳造一連続焼鈍製非時効性ほうろう用鋼板の製造法
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JPH06279864A (ja) * 1993-03-29 1994-10-04 Sumitomo Metal Ind Ltd ほうろう用アルミニウムキルド冷延鋼板の製造方法
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GB9614961D0 (en) * 1996-07-16 1996-09-04 Perkin Elmer Ltd Carrier and its use in the preparation of samples for spectroscopy
WO2001098551A1 (fr) * 2000-06-23 2001-12-27 Nippon Steel Corporation Tole d'acier emaillable a la porcelaine se pretant particulierement bien au formage, au vieillissement et a l'emaillage, et procede de production correspondant
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PL2534271T3 (pl) 2015-10-30
MX348721B (es) 2017-06-26
CN103476955B (zh) 2016-03-30
WO2012136270A1 (fr) 2012-10-11
US20190112684A1 (en) 2019-04-18
EA201391455A1 (ru) 2014-11-28
CN103476955A (zh) 2013-12-25
EP2534271A1 (fr) 2012-12-19
US20190112683A1 (en) 2019-04-18
KR101645786B1 (ko) 2016-08-04
UA111195C2 (uk) 2016-04-11
CA2832357C (fr) 2016-06-07
KR20140014248A (ko) 2014-02-05
MX2013011685A (es) 2014-01-31
US20140065434A1 (en) 2014-03-06
BR112013025885B1 (pt) 2022-05-24
BR112013025885A2 (pt) 2016-12-20
PT2534271E (pt) 2015-10-09
EA024029B1 (ru) 2016-08-31
RS54209B1 (en) 2015-12-31
DK2534271T3 (en) 2015-08-24
SI2534271T1 (sl) 2015-10-30
CA2832357A1 (fr) 2012-10-11
ZA201307344B (en) 2014-11-26
HUE027485T2 (en) 2016-09-28

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