US3522110A - Process for the production of coldrolled steel sheets having excellent press workability - Google Patents

Process for the production of coldrolled steel sheets having excellent press workability Download PDF

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Publication number
US3522110A
US3522110A US616350A US3522110DA US3522110A US 3522110 A US3522110 A US 3522110A US 616350 A US616350 A US 616350A US 3522110D A US3522110D A US 3522110DA US 3522110 A US3522110 A US 3522110A
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Prior art keywords
steel
annealing
content
sheet
drawability
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US616350A
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Mineo Shimizu
Kamematsu Matsuda
Yuzo Sadamura
Nobuyuki Takahashi
Minoru Kawaharada
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Nippon Steel Corp
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Nippon Steel Corp
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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
    • C22C38/14—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
    • B21B1/24—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 in a continuous or semi-continuous process
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • 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

Definitions

  • FIG. 2 Axis density of (III) peak (x random) Average plastic strain ratio (F) MINEO SHIMIZU 'ETAL PROCESS FOR THE PRODUCTION OF COLDROLLED STEEL SHEETS HAVING EXCELLENT PRESS WORKABILITY Filed Feb. 15, 1967 FIG. 2
  • a severe press working for forming parts having complicated shapes from sheet metal by using a punch and a die is usually expressed by the term deep drawing.
  • the deformation of a material in deep drawing is not a simple deformation but a com bination of various factors such as drawing, stretching and bending in various rates.
  • the press formability must be strictly separated into at least drawability and stretchability in accordance with the deforming mode to which the material is subjected.
  • the drawing is characterized by letting the metal at the periphery of a blank (flange portion) flow into a die hole as in the case of forming a cylindrical cup from a circular blank and is called die-drawing.
  • the stretching forms a part having a desired shape by subjecting to a plastic deformation only a section contacted with a punch while preventing the metal at the flange portion of a blank; from being let flow into a die hole by applying a sufilcient blank-holding pressure or providing beads at the flange portion, and is called punch-stretching.
  • the average plastic strain ratio relates to the preferred crystallographic orientation of a material and in the case of steel sheet, if the density of (111) crystal plane and crystal planes near (111) plane accumulated in the rolling plane of the steel sheet is larger and if the density of plane and planes near (100) plane is smaller, the average plastic strain ratio becomes larger.
  • the stretchability is better if an Erichsen value (or Olsen cup value), an elongation by tension test, and a work-hardening exponent are larger, and if an yield point and an yieldtensile ratio are low.
  • drawability and the stretchability relate fundamentally to the chemical composition of steel, the size, shape, and distribution of inclusions contained in the steel, or the crystal grain size and the textures of the steel.
  • a cold-rolled aluminum-killed low-carbon steel sheet for extra deep drawing quality has widely used in practice. Furthermore, there is a low-carbon steel wherein the drawability is improved by adding a specific element such as phosphorus, antimony and molybdenum whereby more (111)-texture preferable for deep drawability is developed at annealing for recrystallization after cold rolling, but such a steel is inferior to the aluminumkilled steel about stretchability.
  • FIG. 1 is a graph showing the influences of heating rates up to annealing temperature on the textures of the cold-rolled steel sheet containing titanium of the present invention, a Ti-containing cold-rolled steel sheet beyond the range of this invention, and an aluminum-killed steel sheet for extra deep drawing quality after annealing,
  • FIG. 2 is a graph showing the influences of the concentration of oxygen in steel on the average plastic strain ratio (7) in the case of subjecting the steel to a con tinuous annealing of 870 C. for 4 min. and to a box annealing of 700 C. for 16 hrs.,
  • FIG. 3 is a graph showing the influences of the concentration of oxygen in steel on the axis density of 111) diffraction peak in the case of subjecting the steel to a continuous annealing of 870 C. for 4 min. and to a box annealing of 700 C. for 16 hrs.,
  • FIG. 4 is a graph showing the influences of the concentration of oxygen in steel on the axis density of (100) diffraction peak in the case of subjecting the steel to a continuous annealing of 870 C. for 4 min. and to a box annealing of 700 C. for 16 hrs., and
  • FIG. 5 is a graph showing the influences of the concentration of oxygen in steel on the total elongation in the case of subjecting the steel to a continuous annealing of 870 C. for 4 min. and to a box annealing of 700 C. for 16 hrs.
  • the chemical composition of the steel of this invention comprises more than 0.001% (by weight) and less than 0.020% C, less than 0.15% 0, more than 0.02% Ti (except Ti as Ti-oxides), said titanium content being more than 4 times larger than carbon content and less than 0.5%, and less than 0.45% Mn, the balance Fe and unavoidable impurities.
  • the content of carbon is preferably less but it is generally impossible in a steel making furnace of an economical scale to reduce the content of carbon less than 0.001%.
  • the content of carbon in steel is reduced by refining in a steel making furnace, the content of oxygen in the molten steel is increased in reverse proportion to the content of carbon, but if the content of oxygen in the steel of this invention is more than 0.015%, the press formability (in particular drawability) is remarkably reduced as will be mentioned below, and in particular, in the case where the steel is heated rapidly to the recrystallizing temperature at annealing, the press formability (in particular drawability) is very remarkably reduced. Accordingly, the content of oxygen in the steel must be reduced below 0.015 by a suitable means.
  • titanium Since titanium is caused to react with carbon, oxygen, nitrogen, sulfur and the like, the content thereof is influenced by the amounts of these ingredients but if the contents of carbon and oxygen are defined as mentioned above and if the steel contains nitrogen and sulfur as impurities in steel obtained conventionally employed various steel manufacturing furnaces (S 0.05%, N 0.007%), it is necessary that the content of titanium 4 except Ti as Ti-oxides thereof be more than 0.020%. It the content of Ti as Ti-oxides is high, (111) texture preferable for deep drawing is not sufflciently developed at annealing for recrystallization even though the steel contains titanium in amount higher than that necessary for stabilizing carbon in the steel, and hence the drawability of the steel is not improved. Further, if the content of titanium is larger than 0.5 the production cost for steel is increased in vain without providing further eflects.
  • manganese is not always necessary in the steel of this invention or the addition of it is undesirable since the average plastic strain ratio tends to be deteriorated by the addition thereof, but if it is necessary to add manganese for making ingots of the steel of this invention, it may be added in an amount of without remarkably deteriorating the average plastic strain ratio or of about 0.45%.
  • the steel of this invention may be produced by any furnace such as a converter, an open-hearth furnace, and an electric furnace, but since the steel containing less than 0.020% of carbon and less than 0.015% of oxygen must be produced, it is profitable in the points of facilitating the practice and improving the titanium yield to conduct a vacuum degassing treatment before ingot making.
  • a deoxydizing agent such as aluminum may be used supplemenetally for adjusting the content of oxygen.
  • the residual aluminum in steel does not influence the properties of the steel of this invention.
  • the steel is formed into ingot, rolled into slabs, if necessary subjected to slab condition, and hot-rolled in which the hot-roll finishing temperature is preferably above 780 C.
  • the steel is then, after pickling, subjected to cold rolling and the cold reduction is desirably, in particular, above 30% for drawability.
  • annealing may be employed box annealing, open-coil annealing or continuous annealing to provide a material having an excellent press workability but by employing a continuous annealing, a particularly excellent steel sheet can be obtained, which is a feature of this invention.
  • the invention is applied to the production of various surface treated steel sheets such as zinc-coated (galvanized) steel sheets, tin plates, aluminized steel sheets, etc., produced by a process including the continuous annealing step, of coarse materials having very excellent press formability.
  • various surface treated steel sheets such as zinc-coated (galvanized) steel sheets, tin plates, aluminized steel sheets, etc.
  • the annealing temperature is from 650 C. to 1000 C., but a preferably annealing temperature is 650-950 C. in the case of box annealing or open-coil annealing and 750-980" C. in the case of continuous annealing.
  • Temper rolling is generally omitted in this invention in the case of employing continuous annealing since the steel of this invention does not have yield point elongation in the as-annealed state but in the case of adjusting the flatness of the sheet or providing a specific surface roughness to the sheet, the temper rolling is conducted with the minimum reduction.
  • Table 1 are shown the chemical compositions of materials used in various examples for explaining the present invention. These materials were hot-rolled into 2.7 mm. in thickness and then cold-rolled into 0.8 mm. in thickness in the conventional process for the production of steel sheet for deep drawing. Two types of annealing were employed in the examples, one of which tightcoil batch annealing under the conditions of 700 C. for 16 hrs. and the other of which was continuous annealing under the conditions of 870 C. for 4 min.
  • the profitability of the continuous annealing consists of two factors.
  • the factors in annealing process which control the development of annealed texture are a heating rate up to annealing temperature, an annealing temperature, and a holding time at the annealing temperature.
  • the development of (111) texture preferable for deep drawability is more remarkable as the heating rate is lower, and hence continuous annealing by rapid heating is unsuitable as an annealing procedure for steel sheet for deep drawing.
  • the development of (111) annealed texture of the cold-rolled steel containing titanium in an amount in the range of this invention is not influenced by the heating rate.
  • the cold-rolled steel containing tita nium in an amount of the range of this invention has a keen susceptibility of the development of (111) texture for annealing conditions and hence the development of (111) texture of the cold-rolled steel sheet of this invention is remarkable as compared with that of a cold-rolled steel sheet containing titanium in an amount beyond the range of this invention.
  • the cold-rolled steel containing titanium in the amount of the range of this invention strongly developes (111) texture in the plane of the sheet even if it is continuousannealed, while a cold-rolled steel containing titanium in an amount beyond the range of this invention and a general cold-rolled low carbon steel do not develop the (111) texture by the reason to be rapidly heated to continuous-annealing temperature.
  • the higher concentrating of (111) planes in the plane of the sheet are developed it the steel is continuous-annealed at higher temperatures which can be attained in only continuous annealing line than in conventional batch-type annealer.
  • the most important factor in this invention is the content of oxygen.
  • the oxygen content in steel is higher than 0.015% by weight, the press formability (in particular drawability) is markedly deteriorated.
  • the relations of the oxygen content with the r value, the intensity of (111) diffraction peak, and the intensity of (100) diffraction peak as the most suitable criterions for drawability are detected from Table 2 and Table 3 and they are shown in FIG. 2, FIG. 3, and
  • FIG. 4 respectively.
  • the 7 value is reduced as the increase of the oxygen content but in particular the change is remarkable at the oxygen content of about 0.015%. Further, this tendency becomes more remarkable in the case of a hightemperature annealing such as the continuous annealing.
  • the greater part of oxygen in the Ti-containing steel sheet is converted into a titanium oxide.
  • the titanium oxide there are various ones such as TiO, Ti O TiO etc., and these oxides have different crystal structures by the kind thereof.
  • the crystal structure and the habit plane of the inhibitor (nitrides, carbides, oxides, etc.) as well as the size and the distribution play an important role. It is commonly considered that when only the influences of the size and the distribution appear as relation as shown in FIG. 2 to FIG. 4, the relation is in linear. Accordingly, the drastic change in the cold rolled sheet steel containing titanium in the amount of the range of this invention at the oxygen content of about 0.015 by weight is not caused by the size and the distribution of the oxides defined by the oxygen content but is assumed to be caused by the change in the composition of titanium oxides in steel. Therefore, it is considered that the oxides existing in an amount of oxygen less than 0.015% does not hinder the growth of the crystal grains (including recrystallizing nuclei) having (111) planes in the plane of the sheet.
  • Such influences by the change of the compositions of the oxides do not appear in the mechanical properties such as stretchability.
  • the elongation is decreased almost linearly as the increase in the oxygen content. This may be due to the reason why the movement of dislocation in plastic deformation and the work-hardening occuring therefrom are most strongly influenced by the size and the distribution of oxides but are scarcely influenced by the oxide composition and the like.
  • the quality of the steel is inferior to that of commercial quality rimmed steel.
  • the lower limit of the titanium content is based on the fundamental concept that the presence of a proper amount of free titanium in steel is a factor for keeping the excellent qualities of the steel of this invention, which is supported by the examples.
  • the cold rolled steel containing titanium in the amount of the range of this invention is a very excellent sheet and has the properties markedly superior to those of conventional steel sheet for deep drawing.
  • a conventional steel sheet is in an annealed state although it is aging steel or non-aging steel, the yield point elongation always appears and hence for removing it temper rolling must be applied.
  • n0 yield point phenomena occurs even if it is annealed by any annealing process (for example, by a batch annealing or continuous annealing) and hence the temper rolling process for preventing the occurrence of stretcher strains is essentially unnecessary.
  • no strain aging of this steel is observed by applying any aging treatment and the yield stress is little influenced by the grain size.
  • the Ti-containing cold rolled steel by the present invention has very excellent properties as compared with conventional steel as the sheet for severe press forming.
  • a process for the production of a cold rolled steel sheet which comprises hot rolling at a temperature higher than 780 C. steel comprising 0.0010.020% (by weight) C, less than 0.45% Mn, less than 0.015% O, and 0.02- 0.5% Ti except Ti as Ti-oxides, said titanium content being higher than four times of the carbon content, the balance Fe and unavoidable impurities, cold rolling it with a reduction of more than 30%, and then annealing it at a temperature of from 650 C. to 1000 C.
  • said steel sheet comprises 0.0010.020% (by weight) C, less than 0.015% O, and 0.02-0.5% Ti except Ti as Ti-oxides, said titanium content being higher than four times of the carbon content, the balance Fe and unavoidable impurities.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
US616350A 1966-02-17 1967-02-15 Process for the production of coldrolled steel sheets having excellent press workability Expired - Lifetime US3522110A (en)

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AT (1) AT307467B (it)
BE (1) BE694190A (it)
DE (1) DE1558720B1 (it)
FR (1) FR1511529A (it)
GB (1) GB1176863A (it)
NL (1) NL6702454A (it)

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3607456A (en) * 1969-04-15 1971-09-21 Bethlehem Steel Corp Deep drawing steel and method of manufacture
DE2324788A1 (de) * 1972-05-19 1973-11-29 Armco Steel Corp Kohlenstoffarmer stahl und verfahren zu seiner herstellung
US3792999A (en) * 1971-02-05 1974-02-19 Hoerder Huettenunion Ag Method of producing a drawing and deep drawing steel resistant to ageing, particularly for single-coat enamelling
US3798076A (en) * 1971-04-27 1974-03-19 Nippon Steel Corp METHOD FOR PRODUCING Al-KILLED DEEP DRAWING COLD ROLLED STEEL PLATE BY CONTINUOUS ANNEALING
US3897280A (en) * 1972-12-23 1975-07-29 Nippon Steel Corp Method for manufacturing a steel sheet and product obtained thereby
US3926692A (en) * 1974-09-30 1975-12-16 United States Steel Corp Drawability of deoxidized steels by the addition of phosphorus and silicon
US4119445A (en) * 1971-05-10 1978-10-10 Youngstown Sheet And Tube Company High strength alloy of ferritic structure
US4124412A (en) * 1971-01-18 1978-11-07 Armco Steel Corporation Columbium treated, non-aging, vacuum degassed low carbon steel and method for producing same
DE2942338A1 (de) * 1978-10-21 1980-04-24 Nippon Steel Corp Verfahren zur herstellung von alterungsbestaendigem kaltgewalztem stahlband
USRE30851E (en) * 1969-12-30 1982-01-19 Nippon Steel Corporation Method for producing low-carbon cold rolled steel sheet having excellent cold working properties and an apparatus for continuous treatment thereof
EP0048351A1 (en) * 1980-08-27 1982-03-31 Nippon Steel Corporation High strength cold rolled steel strip having an excellent deep drawability
EP0067878A1 (en) * 1980-11-26 1982-12-29 Kawasaki Steel Corporation Method of manufacturing thin steel plate for drawing with baking curability
FR2513267A1 (fr) * 1981-09-18 1983-03-25 Nippon Steel Corp Procede de fabrication de toles et de bandes en acier laminees a froid a etirage profond
EP0108268A1 (en) * 1982-10-08 1984-05-16 Nippon Steel Corporation Method for the production of cold rolled steel sheet having super deep drawability
EP0231864A2 (de) * 1986-02-06 1987-08-12 Hoesch Stahl Aktiengesellschaft Alterungsfreier Bandstahl
CN114107639A (zh) * 2021-11-25 2022-03-01 包头钢铁（集团）有限责任公司 一种普通级稀土取向硅钢制备方法

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ZA71834B (en) * 1970-03-02 1972-04-26 Armco Steel Corp Columbium treated non-aging vacuum degassed low carbon steel and method for producing same
JPS5722974B2 (it) * 1975-01-28 1982-05-15
JPS5825436A (ja) * 1981-08-10 1983-02-15 Kawasaki Steel Corp 遅時効性、異方性小なる深絞り用冷延鋼板の製造方法
NL8800391A (nl) * 1988-02-17 1989-09-18 Hoogovens Groep Bv Verouderingsbestendig laaggelegeerd warmgewalst bandvormig vervormingsstaal.

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3183078A (en) * 1961-09-29 1965-05-11 Yawata Iron & Steel Co Vacuum process for producing a steel for nonageing enameling iron sheets
US3303064A (en) * 1963-11-29 1967-02-07 Inland Steel Co Alloy steel article and method of producing
US3420718A (en) * 1964-08-22 1969-01-07 Yawata Seitetsu Kk Process for the production of very low carbon-containing cold-rolled steel strips

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2597979A (en) * 1949-12-21 1952-05-27 United States Steel Corp Recrystallizing deep-drawing steel

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3183078A (en) * 1961-09-29 1965-05-11 Yawata Iron & Steel Co Vacuum process for producing a steel for nonageing enameling iron sheets
US3303064A (en) * 1963-11-29 1967-02-07 Inland Steel Co Alloy steel article and method of producing
US3420718A (en) * 1964-08-22 1969-01-07 Yawata Seitetsu Kk Process for the production of very low carbon-containing cold-rolled steel strips

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3607456A (en) * 1969-04-15 1971-09-21 Bethlehem Steel Corp Deep drawing steel and method of manufacture
USRE30851E (en) * 1969-12-30 1982-01-19 Nippon Steel Corporation Method for producing low-carbon cold rolled steel sheet having excellent cold working properties and an apparatus for continuous treatment thereof
US4124412A (en) * 1971-01-18 1978-11-07 Armco Steel Corporation Columbium treated, non-aging, vacuum degassed low carbon steel and method for producing same
US3792999A (en) * 1971-02-05 1974-02-19 Hoerder Huettenunion Ag Method of producing a drawing and deep drawing steel resistant to ageing, particularly for single-coat enamelling
US3798076A (en) * 1971-04-27 1974-03-19 Nippon Steel Corp METHOD FOR PRODUCING Al-KILLED DEEP DRAWING COLD ROLLED STEEL PLATE BY CONTINUOUS ANNEALING
US4119445A (en) * 1971-05-10 1978-10-10 Youngstown Sheet And Tube Company High strength alloy of ferritic structure
DE2324788A1 (de) * 1972-05-19 1973-11-29 Armco Steel Corp Kohlenstoffarmer stahl und verfahren zu seiner herstellung
US3897280A (en) * 1972-12-23 1975-07-29 Nippon Steel Corp Method for manufacturing a steel sheet and product obtained thereby
US3926692A (en) * 1974-09-30 1975-12-16 United States Steel Corp Drawability of deoxidized steels by the addition of phosphorus and silicon
DE2942338A1 (de) * 1978-10-21 1980-04-24 Nippon Steel Corp Verfahren zur herstellung von alterungsbestaendigem kaltgewalztem stahlband
EP0048351A1 (en) * 1980-08-27 1982-03-31 Nippon Steel Corporation High strength cold rolled steel strip having an excellent deep drawability
EP0067878A1 (en) * 1980-11-26 1982-12-29 Kawasaki Steel Corporation Method of manufacturing thin steel plate for drawing with baking curability
EP0067878A4 (en) * 1980-11-26 1984-01-09 Kawasaki Steel Co METHOD FOR PRODUCING A THIN DEEP-DRAWING STEEL SHEET WITH HIGH TURNABILITY BY HEATING TO BURNING TEMPERATURE.
FR2513267A1 (fr) * 1981-09-18 1983-03-25 Nippon Steel Corp Procede de fabrication de toles et de bandes en acier laminees a froid a etirage profond
EP0108268A1 (en) * 1982-10-08 1984-05-16 Nippon Steel Corporation Method for the production of cold rolled steel sheet having super deep drawability
EP0231864A2 (de) * 1986-02-06 1987-08-12 Hoesch Stahl Aktiengesellschaft Alterungsfreier Bandstahl
DE3603691A1 (de) * 1986-02-06 1987-08-20 Hoesch Stahl Ag Alterungsfreier bandstahl
EP0231864A3 (en) * 1986-02-06 1989-04-26 Hoesch Stahl Aktiengesellschaft Non-ageing steel strip
CN114107639A (zh) * 2021-11-25 2022-03-01 包头钢铁（集团）有限责任公司 一种普通级稀土取向硅钢制备方法

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FR1511529A (fr) 1968-01-26
DE1558720A1 (it) 1973-05-10
GB1176863A (en) 1970-01-07
AT307467B (de) 1973-04-15
DE1558720B1 (de) 1973-05-10
BE694190A (it) 1967-07-31
NL6702454A (it) 1967-08-18

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