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EP3959021B1 - Verfahren zur herstellung eines hochfesten siliciumhaltigen stahlbandes mit ausgezeichneter oberflächenqualität und dadurch hergestelltes, besagtes stahlband - Google Patents

Verfahren zur herstellung eines hochfesten siliciumhaltigen stahlbandes mit ausgezeichneter oberflächenqualität und dadurch hergestelltes, besagtes stahlband Download PDF

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Publication number
EP3959021B1
EP3959021B1 EP20717067.1A EP20717067A EP3959021B1 EP 3959021 B1 EP3959021 B1 EP 3959021B1 EP 20717067 A EP20717067 A EP 20717067A EP 3959021 B1 EP3959021 B1 EP 3959021B1
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Prior art keywords
strip
hot
rolled
rolling
slab
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French (fr)
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EP3959021A1 (de
Inventor
Wanda Maria Carolina MELFO PRADA
Mattheüs Hendrik Marinus HUISERT
Albert Edgar WESTENDORP
Richard Alexander VAN DOK
Koert VAN EIJK
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Tata Steel Ijmuiden BV
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Tata Steel Ijmuiden BV
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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
    • B21B1/46—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 metal immediately subsequent to continuous casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/04—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing
    • B21B45/06—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing of strip material
    • 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
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel

Definitions

  • This invention relates to a method for producing a high strength sheet silicon containing steel strip with excellent surface quality of the hot-rolled product.
  • Hot rolled strips of steels containing elevated levels of silicon in combination or not with other elements often has poor surface quality after hot-rolling.
  • the poor surface quality is related to the presence of Si which forms brittle oxide scales that, after fracturing in the roll bite, are rolled into the steel surface during the finishing rolling process.
  • a typical threshold level of silicon for these surface issues to occur is 0.10 wt.%.
  • the steels with mentioned compositions are cast in a slab, then reheated to temperatures in a range of 1200 to 1300°C and then descaled, rough-rolled to form a transfer bar, descaled again and finish-rolled to the end thickness.
  • the strip is then cooled in a run-out-table and coiled.
  • the obtained product can be already of high strength and finished with a hot-dip galvanised coating; or further pickled, cold rolled, annealed and optionally coated, e.g. by hot dip galvanising.
  • CN102764760 discloses a method for manufacturing a high surface quality hot-rolled steel plate with a silicon content below 0.15 wt.%.
  • US2015/0243418-A1 discloses a hot rolled silicon steel producing method wherein the heating process and the rough rolling process are changed so that the occurrence rate of edge defects during the production of the hot rolled silicon steel can be reduced, and the hot rolled silicon steel with good surface quality can be produced.
  • US5235840 a system for processing steel strips in a hot strip mill including an apparatus and method for minimizing oxide growth on steel strips and reducing wear on work rolls in the finishing mill is disclosed.
  • JPH11156407 provides a method for manufacturing a hot rolled steel sheet of high Si excellent in surface quality with less red scale flaw by tailoring the descaling method.
  • US 2010/218911 A1 discloses a method to produce hot-rolled steel strips from continuously cast thick or thin slabs comprising Si of 0,23 wt.% and 1,43 wt.% Mn, the method comprising heating or reheating the slab to a reheating temperature of at least 1100 °C in a reheating or homogenising furnace, optionally hot-rolling the slab to a transfer bar in a roughing mill consisting of one or more rough rolling stands, transferring the transfer bar to a tandem finishing mill consisting of a plurality of finishing mill rolling stands, descaling the transfer bar in a descaler, and rolling the descaled transfer bar in said plurality of finishing mill rolling stands to a hot-rolled strip having a final thickness of less than about 8.0 mm.
  • One or more objectives are reached with a method to produce hot-rolled steel strips from continuously cast thick or thin slabs comprising Si between 0.10 and 3.00 wt.% and at least 0.8 wt.% Mn comprising heating or reheating the slab to a reheating temperature of at least 1100 °C in a reheating or homogenising furnace, optionally hot-rolling the slab to a transfer bar in a roughing mill consisting of one or more rough rolling stands, transferring the transfer bar to a tandem finishing mill consisting of a plurality of finishing mill rolling stands, descaling the transfer bar in a descaler, and rolling the descaled transfer bar in said plurality of finishing mill rolling stands to a hot-rolled strip having a final thickness wherein the temperature of the strip at exit of the last stand in the finishing mill rolling T is determined by T (°C) > 41.823 In(wt.% Si) + 980.4 and the time between the descaler and the first finishing mill rolling stand td-F1 is determined by td-F
  • the descaler in which the transfer bar is descaled before finish rolling is the last descaling unit before the finishing mill.
  • additional descaling units are fitted, e.g. to descale the reheated slabs prior to rough rolling of the slab.
  • these additional units do not descale the transfer bar, but (e.g.) the reheated thick slab.
  • the descaling unit for descaling the reheated slab is also the last descaler unit before the finishing mill.
  • cooling actuators is effective for controlling the surface of LC-LA steels and it is common practice in all hot strip mills.
  • the formation of higher proportions of higher oxides in the steels containing more than 0.10 wt.% Si cannot be avoided by lowering the temperatures during finish rolling.
  • the limit of plasticity of the oxide layer depends on the actual thickness of the brittle oxides available, which are proportional and depend on the steel composition.
  • Figure 1 shows a schematic drawing of the approximate transition of ductile to brittle when reducing the temperature.
  • the oxide scale is ductile at high temperature. If this is combined with a thin scale, then the hematite layer does not act as crack initiator. As soon as the temperature is approx. below 920°C, the magnetite (Fe 3 O 4 ) is no longer able to accommodate the elongation and it can break, therefore below 920°C in this temperature region the magnetite layer thickness dominates the fracture mode. When the whole oxide scale is below the ductility limit for all oxides (i.e. approx. below 600°C) then the oxide will break already under a very small load. Hematite (Fe 2 O 3 ) is brittle for the full practical range of hot-rolling temperatures.
  • the method according to the invention is based on promoting the presence of the ductile magnetite and wüstite (FeO) and avoiding hematite.
  • the inventors have developed a method to determine the plasticity limit based on the oxide thickness entering each stand in the finishing mill and the surface temperature. This is achieved by starting the finish rolling process immediately after descaling the transfer bar at a high speed (v) and a high surface temperature of the transfer bar (T), preferably without the use of cooling actuators in the finishing mill. These measures ensure that the temperature stays high enough during finishing rolling to ensure that the oxide is sufficiently ductile.
  • the method according to the invention ensures that the surface quality is not only excellent, but also uniform. This means that if the hot rolled strip is subsequently pickled and cold-rolled, that the surface remains excellent and uniform, and this positively affects the surface quality of the coated product after providing the finished product with a metallic coating.
  • the limit line in Figure 3 was calculated based on the surface quality results. These results are obtained from the surface inspection system located after the last stand on the finishing mill.
  • the triangles represent sampling locations on a strip that have poor surface quality after hot rolling, the circles represent a good surface quality after hot rolling.
  • the X-axis corresponds to the calculated surface temperature of the strip at the entry of the roll bite and the Y-axes is the equivalent calculated oxide scale thickness at the corresponding roll bite.
  • the surface temperature calculation was obtained from our own off-line simulator of the finishing mill, which takes into account the heat losses due to convection and radiation using the industrial coil parameters.
  • the optionality of the hot-rolling of the slab to a transfer bar in a roughing mill consisting of one or more rough rolling stands relates to the differences in set-up of the available hot strip production facilities.
  • the conventional hot strip mill generally consists of one or more reheating furnaces to reheat thick slabs with a thickness of between about 150 and 350 mm to a high temperature. These and following dimensions in relation to the hot strip production facilities are indications and not intended to be limiting.
  • the reheated slabs are subsequently descaled for the first time to remove the furnace scale and processed in a roughing mill comprising one or more rolling stands and reduced in thickness to about 35 to 40 mm.
  • the rough-rolled slab is now generally referred to as a transfer bar.
  • This transfer bar is rolled to its final hot-rolled thickness in a multi-stand finishing mill.
  • the slab Prior to this finish rolling the slab is again descaled to remove the scale that formed on the transfer bar in the period between roughing and the delay time before finish rolling.
  • finish rolling the strip is cooled to the coiling temperature on the run-out table and coiled.
  • An example of such a facility is the HSM#2 of Tata Steel in IJmuiden.
  • the rolling mill consists of a roughing mill, comprising one or more rolling stands and a multi-stand finishing mill.
  • the thin cast slab has a thickness of below 150 mm, generally in the range of 35 to 80 mm.
  • This strip is fed directly from the caster into a homogenising furnace and (re-)heated or homogenised to a high temperature.
  • These thin cast slabs are subsequently descaled for the first time to remove the furnace scale and processed in a roughing mill comprising one or more rolling stands and reduced in thickness.
  • the rough-rolled slab could now be referred to as a transfer bar but is much thinner than the one in the conventional hot strip mill.
  • This transfer bar is rolled to its final hot-rolled thickness in a multi-stand finishing mill.
  • the slab Prior to this finish rolling the slab is again descaled to remove the scale that formed on the transfer bar in the period between roughing and the delay time before finish rolling.
  • finish rolling the strip is cooled to the coiling temperature on the run-out table and coiled.
  • An example of such a facility is the thin slab caster and direct rolling facility of Tata Steel in IJmuiden.
  • the rolling mill only consists of a multi-stand finishing mill.
  • the thin cast slabs are descaled to remove the furnace scale and immediately processed to its final hot-rolled thickness in the multi-stand finishing mill.
  • the descaled thin cast slab is the transfer bar.
  • the descaler after the homogenisation furnace may be the only descaling between (re-)heating and finish-rolling. After finish rolling the strip is cooled to the coiling temperature on the run-out table and coiled.
  • An example of such a facility is the CSP thin slab caster and direct rolling facility of thyssenkrupp Steel in Duisburg.
  • the steel strip has a composition comprising (in wt.%) C: 0.010 - 0.50 P: ⁇ 0.100 Nb: ⁇ 0.30 Mn: 0.80 - 6.00 S: ⁇ 0.050 V: ⁇ 0.50 N: 0.001 - 0.030 B: ⁇ 0.0100 Ca: ⁇ 0.050 Si: 0.10 - 3.00 O: ⁇ 0.008 Ni ⁇ 2.0 Cr: ⁇ 4.00 Ti: ⁇ 0.30 Cu ⁇ 2.0 Al: ⁇ 3.00 Mo: ⁇ 1.00 W ⁇ 0.50 the remainder being iron and unavoidable impurities.
  • any one or more of the optional elements may also be absent. i.e. either the amount of the element is 0 wt.% or the element is present as an unavoidable impurity.
  • the steel strip has a composition comprising (in wt.%) C: 0.040 - 0.25 P: ⁇ 0.020 Nb: ⁇ 0.30 Mn: 0.80 - 3.00 S: ⁇ 0.005 V: ⁇ 0.50 N: ⁇ 0.0120 B: ⁇ 0.0050 Ca: ⁇ 0.050 Si: ⁇ 0.10-2.00 O: ⁇ 0.008 Ni ⁇ 0.050 Cr: ⁇ 1.00 Ti: ⁇ 0.30 Cu ⁇ 0.050 Al: ⁇ 1.50 Mo: ⁇ 0.50 W ⁇ 0.020 the remainder being iron and unavoidable impurities.
  • Typical high strength steel grades are given in table A.
  • the steel strip has a composition comprising (in wt.%) C: 0.10 - 0.25 P: ⁇ 0.020 Nb: ⁇ 0.30 Mn: 1.40 - 2.40 S: ⁇ 0.005 V: ⁇ 0.50 N: ⁇ 0.0100 B: ⁇ 0.0050 Ca: ⁇ 0.050 Si: ⁇ 0.10-0.40 O: ⁇ 0.008 Ni ⁇ 0.050 Cr: ⁇ 1.00 Ti: ⁇ 0.30 Cu ⁇ 0.050 Al: ⁇ 1.50 Mo: ⁇ 0.50 W ⁇ 0.020 the remainder being iron and unavoidable impurities.
  • the silicon content is the main contributing factor of the chemical composition in the method according to the invention
  • the ranges of the other elements are interchangeable and can be considered independently in the light of the problem that is solved by this invention.
  • the other elements affect other properties, like the mechanical properties, but from the surface quality point of view they are independent features.
  • the surface appearance of the hot-rolled steel strip is uniform along width and length of the strip.
  • the principle of the method is based on a centreline measurement as described, but as it is the intention that the processing conditions are as homogeneous as possible over the width and length of the strip, the preferred embodiment should guarantee the uniformity of the surface appearance over the width and length of the strip.
  • the transfer bar is descaled immediately prior to entering the first finishing mill rolling stand. This ensures that the surface of the transfer bar is free from oxide at the start of the finish rolling. To further prevent the formation of sticking oxide, it is preferable that the cast thick or thin slab is descaled immediately prior to entering the first roughing mill rolling stand.
  • a hot rolled strip generally refers to a steel product, usually supplied as a coiled product.
  • the strip thickness can be between 1 and 25 mm, depending on the supplier and the type of application for the steel. Strips can be cut into smaller segments, such as sheets.
  • the thickness of the strip in the method according to the invention is less than about 8.0 mm, or less than 7.0 mm, or less than 6.0 mm or less than 5.0 mm.
  • the steel strip or sheet produced according to the invented method has a thickness of at most 4.0 mm.
  • the steel strip can be used in its hot rolled state, or as pickled and oiled strip, but in many cases the steel strip will be protected against corrosion by the application of a coating layer.
  • the hot-rolled strip is provided with a metallic coating by hot-dip coating or by electroplating or with a coating by physical vapour deposition. In most cases the hot rolled strip is pickled before application of the coating hot-rolled scale from the surface of the strip.
  • the coating that is applied by physical vapour deposition is usually a metallic coating, but it can also be a non-metallic coating.
  • the hot-rolled strip produced according to the invention is subsequently cold-rolled to a cold rolled strip.
  • the hot rolled strip is pickled before application cold-rolling to remove the hot-rolled scale from the surface of the strip.
  • the hot-rolled strip is cold-rolled to a cold rolled strip and subsequently annealed to produce an annealed strip having a recrystallised or recovered microstructure.
  • the cold rolled and subsequently annealed strip is subsequently provided with a metallic coating by hot-dip coating, by electroplating or with a coating by physical vapour deposition.
  • the coating that is applied by physical vapour deposition is usually a metallic coating, but it can also be a non-metallic coating.
  • the metallic coating is selected from the group of coatings comprising or consisting of (Zn, Zn-AI, Zn-Mg-Al, Al-Si, Sn, Cr, Ni).
  • the invention is also embodied in hot-rolled strip produced according to the method according to the invention or in a cold-rolled steel strip produced according to the method according to the invention.
  • Table A Typical high strength steel grades (wt.%) Steel C Si Mn Cr Al Ti B N V A 0.09 0.25 1.6 0.5 0.03 0.02 0.0005 0.005 0.03 B 0.12 0.25 1.82 0.6 0.03 0.02 0.0005 0.005 0.03 C 0.15 0.1 2.1 0.1 0.7 0.02 0.002 0.005 0.03 D 0.15 0.4 2.1 0.5 0.6 0.02 0.002 0.005 0.03 E 0.16 0.1 2.4 0.5 0.03 0.04 0.0005 0.005 0.03 F 0.22 1.8 2.1 0.1 0.03 0.04 0.0005 0.005 0.03
  • the limit values for a good surface quality can be found.
  • Three main variables define the procedure to avoid oxide fracture: Si content in the steel (Si, wt.%), time between the descaler and the first stand of the finishing mill (t d-F1 , s) and the average temperature along the coil at exit of the finishing mill (T, °C). Time and temperature are measured over the centre line of the mill, and thus of the strip. The temperature over the width should preferably be as homogeneous as possible, and preferably similar to the centreline value. This way the chance that the edges and the centre of the strip have good surface quality is maximised.
  • a strip produced as such that satisfy both of the following conditions will have good surface at the locations where these conditions are met: T ° C > 41.823 ln wt . % Si + 980.4 t d ⁇ F 1 s ⁇ ⁇ 0.603 ln wt . % Si + 4.8731
  • the range of Si is between 0.10 wt.% to 3.00 wt.%. Wherever these conditions are met, a good surface quality could be expected.
  • the temperature of the strip at exit of the finishing mill and thus the average temperature along the coil at exit of the finishing mill is a direct consequence of the entry temperature, and the entry speed and any cooling during and in between stands.
  • Variables such as the final thickness of the strip and the reduction schedule in the various rolling stands of the finishing mill are used as input for determining the time between the descaler and F1 and the entry temperature to arrive at the desired exit temperature.
  • Figure 4 gives an example of a good (top image) and a bad quality (bottom image).
  • the steel was a 0.14%C; 2.1%Mn; 0.2%Si; 0.25%Cr steel.
  • the steel in the top image was produced under the conditions prescribed by equations (1) and (2), and the steel in the bottom image was not.
  • the difference in surface quality is striking.
  • the surface quality of the steel in the top image is perfectly suited to be processed further, whereas the surface quality of the steel in the bottom image is such that repair of the surface during further processing is virtually impossible.
  • the steel in the bottom image is very likely to be rejected or downgraded.

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  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Metal Rolling (AREA)
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Claims (15)

  1. Verfahren zur Herstellung von warmgewalzten Stahlbändern aus stranggegossenen dicken oder dünnen Brammen, die Si zwischen 0,10 und 3,00 Gew.-% und mindestens 0,80 Gew.-% Mn umfassen, wobei das Verfahren das Erwärmen oder Wiedererwärmen der Bramme auf eine Wiedererwärmungstemperatur von mindestens 1100 °C in einem Wiedererwärmungs- oder Homogenisierungsofen, optional das Warmwalzen der Bramme zu einem Vorband in einem Vorwalzwerk, das aus einem oder mehreren Vorwalzgerüsten besteht, das Übertragen der Bramme oder des Vorbandes zu einem Tandem-Fertigwalzwerk, das aus einer Vielzahl von Fertigwalzgerüsten besteht, das Entzundern der Bramme oder des Vorbandes in einem Entzunderer und das Walzen der entzunderter Bramme oder des entzunderten Vorbandes in der Vielzahl von Fertigwalzgerüsten zu einem warmgewalzten Band mit einer Enddicke von weniger als etwa 8,0 mm umfasst, wobei die Temperatur des Bandes am Ausgang des letzten Gerüsts in dem Fertigwalzwerk T bestimmt wird von T (°C) > 41,823 ln(Gew.-% Si) + 980,4 und die Zeit zwischen dem Entzunderer und dem ersten Fertigwalzwerkgerüst td-F1 bestimmt wird von td-F1 (s) < -0,603 ln(Gew.-% Si) + 4,8731.
  2. Verfahren nach Anspruch 1, wobei das Verfahren das Warmwalzen der Bramme zu einem Vorband in einem Vorwalzwerk, das aus einem oder mehreren Vorwalzgerüsten besteht, umfasst.
  3. Verfahren nach Anspruch 1 oder 2, wobei das Stahlband eine Folgendes umfassende Zusammensetzung (in Gew.-%) aufweist C: 0,040 - 0,25 P: ≤ 0,020 Nb: ≤ 0,30 Mn: 0,80 - 3,00 S: ≤ 0,005 V: ≤ 0,50 N: ≤ 0,0120 B: ≤ 0,0050 Ca: ≤ 0,050 Si: ≤ 0,10-2,00 O: ≤ 0,008 Ni ≤ 0,050 Cr: ≤ 1,00 Ti: ≤ 0,30 Cu ≤ 0,050 Al: ≤ 1,50 Mo: ≤ 0,50 W ≤ 0,020
    wobei der Rest Eisen und unvermeidbare Verunreinigungen ist.
  4. Verfahren nach einem der vorhergehenden Ansprüche, wobei das Oberflächenaussehen des warmgewalzten Stahlbandes entlang der Breite und Länge des Bandes gleichförmig ist.
  5. Verfahren nach einem der vorhergehenden Ansprüche, wobei die Bramme oder das Vorband unmittelbar vor dem Eintreten in das erste Fertigwalzgerüst entzundert wird.
  6. Verfahren nach Anspruch 2 oder einem der Ansprüche 3 bis 5 when abhängig von Anspruch 2, wobei die gegossene dicke oder dünne Bramme unmittelbar vor dem Eintreten in das erste Vorwalzgerüst entzundert wird.
  7. Verfahren nach einem der vorhergehenden Ansprüche, wobei die Enddicke des warmgewalzten Bandes höchstens 4,0 mm beträgt.
  8. Verfahren nach einem der vorhergehenden Ansprüche, wobei das warmgewalzte Band mit einer metallischen Beschichtung durch Schmelztauchbeschichtung oder durch Elektroplattieren oder mit einer Beschichtung durch physikalische Dampfabscheidung versehen wird.
  9. Verfahren nach einem der vorhergehenden Ansprüche, wobei das warmgewalzte Band zu einem kaltgewalzten Band kaltgewalzt wird.
  10. Verfahren nach einem der vorhergehenden Ansprüche, wobei das warmgewalzte Band zu einem kaltgewalzten Band kaltgewalzt und anschließend geglüht wird, um ein geglühtes Band mit einer rekristallisierten oder rückgewonnenen Mikrostruktur herzustellen.
  11. Verfahren nach einem der vorhergehenden Ansprüche, wobei das warmgewalzte Band zu einem kaltgewalzten Band kaltgewalzt und anschließend geglüht wird, ein geglühtes Band mit einer rekristallisierten oder rückgewonnenen Mikrostruktur herzustellen, das anschließend mit einer metallischen Beschichtung durch Schmelztauchbeschichtung, durch Elektroplattieren oder durch physikalische Dampfabscheidung versehen wird.
  12. Verfahren nach Anspruch 8, wobei das kaltgewalzte und optional geglühte Band mit einer metallischen Beschichtung durch Elektroplattieren versehen wird.
  13. Verfahren nach dem Anspruch 8 oder 11, wobei die Beschichtung ausgewählt ist aus der Gruppe von Beschichtungen bestehend aus (Zn, Zn-Al, Zn-Mg-Al, Al-Si).
  14. Verfahren nach dem Anspruch 12, wobei die Beschichtung ausgewählt ist aus der Gruppe von Beschichtungen bestehend aus (Zn, Zn-Al, Zn-Mg-Al, Al-Si, Sn).
  15. Verfahren nach einem der vorhergehenden Ansprüche, wobei das warmgewalzte Stahlband nach dem Abkühlen auf Umgebungstemperaturen und vor dem optionalen Kaltwalzen gebeizt wird, um die Oxide von der Oberfläche zu entfernen, um eine gleichförmige und oxidfreie Oberfläche ohne Restzunder zu erhalten.
EP20717067.1A 2019-04-20 2020-04-17 Verfahren zur herstellung eines hochfesten siliciumhaltigen stahlbandes mit ausgezeichneter oberflächenqualität und dadurch hergestelltes, besagtes stahlband Active EP3959021B1 (de)

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EP19170439 2019-04-20
PCT/EP2020/060867 WO2020216686A1 (en) 2019-04-20 2020-04-17 Method for producing a high strength silicon containing steel strip with excellent surface quality and said steel strip produced thereby

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EP3959021A1 EP3959021A1 (de) 2022-03-02
EP3959021B1 true EP3959021B1 (de) 2022-08-24

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Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0377734A1 (de) * 1987-03-11 1990-07-18 Nippon Kokan Kabushiki Kaisha Verfahren zur herstellung von nichtorientiertem stahlblech mit hohem siliziumgehalt
US5001915A (en) 1986-09-22 1991-03-26 David T. Blazevic Method for improving hot strip mill processing
JPH11267741A (ja) 1998-03-19 1999-10-05 Kobe Steel Ltd 表面性状の優れた熱延鋼板の製造方法
JP2005297008A (ja) 2004-04-13 2005-10-27 Nippon Steel Corp 表面性状の良好な高Ｓｉ含有鋼板の熱間圧延方法
JP3781344B2 (ja) 1999-11-12 2006-05-31 新日本製鐵株式会社 バーリング加工性と疲労特性に優れた熱延鋼板の製造方法
US20100218911A1 (en) 2007-12-11 2010-09-02 Chao Zhang Method and system for producing wide steel strip
JP5326709B2 (ja) 2008-04-03 2013-10-30 新日鐵住金株式会社 低降伏比型高バーリング性高強度熱延鋼板及びその製造方法
JP6288321B2 (ja) 2014-02-05 2018-03-07 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61206507A (ja) * 1985-03-12 1986-09-12 Ishikawajima Harima Heavy Ind Co Ltd 冷延鋼板製造設備
US5235840A (en) 1991-12-23 1993-08-17 Hot Rolling Consultants, Ltd. Process to control scale growth and minimize roll wear
JPH11156407A (ja) 1997-11-28 1999-06-15 Sumitomo Metal Ind Ltd 表面品質の優れた熱延鋼板の製造方法
DE102007005015A1 (de) * 2006-06-26 2008-01-03 Sms Demag Ag Verfahren und Anlage zur Herstellung von Warmband-Walzgut aus Siliziumstahl auf der Basis von Dünnbrammen
CN103302104B (zh) 2012-03-13 2015-07-22 宝山钢铁股份有限公司 热轧硅钢的制造方法
CN102764760A (zh) 2012-07-03 2012-11-07 南京钢铁股份有限公司 一种高表面质量热轧钢板的制造方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5001915A (en) 1986-09-22 1991-03-26 David T. Blazevic Method for improving hot strip mill processing
EP0377734A1 (de) * 1987-03-11 1990-07-18 Nippon Kokan Kabushiki Kaisha Verfahren zur herstellung von nichtorientiertem stahlblech mit hohem siliziumgehalt
JPH11267741A (ja) 1998-03-19 1999-10-05 Kobe Steel Ltd 表面性状の優れた熱延鋼板の製造方法
JP3781344B2 (ja) 1999-11-12 2006-05-31 新日本製鐵株式会社 バーリング加工性と疲労特性に優れた熱延鋼板の製造方法
JP2005297008A (ja) 2004-04-13 2005-10-27 Nippon Steel Corp 表面性状の良好な高Ｓｉ含有鋼板の熱間圧延方法
US20100218911A1 (en) 2007-12-11 2010-09-02 Chao Zhang Method and system for producing wide steel strip
JP5326709B2 (ja) 2008-04-03 2013-10-30 新日鐵住金株式会社 低降伏比型高バーリング性高強度熱延鋼板及びその製造方法
JP6288321B2 (ja) 2014-02-05 2018-03-07 Ｊｆｅスチール株式会社 高強度熱延鋼板およびその製造方法

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
AMINE ALAOUI MOUAYD , ALEXEY KOLTSOV , ELIANE SUTTER , BERNARD TRIBOLLET: "Effect of silicon content in steel and oxidation temperature on scale growth and morphology", MATERIALS CHEMISTRY AND PHYSICS, vol. 143, pages 996 - 1004, XP028807610, DOI: 10.1016/j.matchemphys.2013.10.037
HIKARU OKADA ET AL.: "Prevention of Red Scale Formation during Hot-rolling of Steels", ISIJ INTERNATIONAL, vol. 35, no. 7, 1995, pages 886 - 891, XP055758885, DOI: 10.2355/isijinternational.35.886
YUAN QING, XU GUANG, ZHOU MINGXING, HE BEI: "The Effect of the Si Content on the Morphology and Amount of Fe2SiO4 in Low Carbon Steels", METALS, vol. 6, no. 94, 22 April 2016 (2016-04-22), CH , pages 1 - 9, XP093139900, ISSN: 2075-4701, DOI: 10.3390/met6040094

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