WO1997024465A1 - Fer noir doux obtenu par recuisson en continu et laminage, pour la fabrication de recipients par emboutissage et etirage/emboutissage profond - Google Patents

Fer noir doux obtenu par recuisson en continu et laminage, pour la fabrication de recipients par emboutissage et etirage/emboutissage profond Download PDF

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Publication number
WO1997024465A1
WO1997024465A1 PCT/KR1996/000260 KR9600260W WO9724465A1 WO 1997024465 A1 WO1997024465 A1 WO 1997024465A1 KR 9600260 W KR9600260 W KR 9600260W WO 9724465 A1 WO9724465 A1 WO 9724465A1
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Prior art keywords
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blackplates
manufacturing
steel
temperature
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PCT/KR1996/000260
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English (en)
Inventor
Jai Hyun Kwak
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Pohang Iron & Steel Co., Ltd.
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Application filed by Pohang Iron & Steel Co., Ltd. filed Critical Pohang Iron & Steel Co., Ltd.
Priority to JP9524236A priority Critical patent/JPH10505882A/ja
Priority to DE19681270T priority patent/DE19681270T1/de
Publication of WO1997024465A1 publication Critical patent/WO1997024465A1/fr

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Classifications

    • 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
    • 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
    • C21D8/0405—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 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • 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

Definitions

  • the present invention relates to a soft temper blackplates used as a raw material for tinplates (tin coated steel sheets) or tin free steel sheet for drawn and ironed cans and deep-drawn vessels such as 2-piece cans, camping gas cans, shells of dry cells and the like, and a manufacturing method therefor.
  • the present invention relates to a continuously annealed blackplates for drawn and ironed cans (hereafter "D&I cans”) and deep drawn vessels, and manufacturing method therefor, which is manufactured through a continuous annealing, and in which a superior drawing for ability and stable material properties are ensured.
  • D&I cans continuously annealed blackplates for drawn and ironed cans
  • manufacturing method therefor which is manufactured through a continuous annealing, and in which a superior drawing for ability and stable material properties are ensured.
  • a continuous annealing is carried out at a high temperature so as to give good formability of steel sheets, and the deterioration of mechanical properties by aging is inhibited through an over-aging and a skinpass.
  • the additive elements cannot be sufficiently added due the apprehension that the recrystallization temperature might be raised. Further, the recrystallization temperature is greatly varied depending on the hot rolling conditions and the content of impurity elements, particularly the content of S, and therefore, a stable material cannot be obtained.
  • the present inventor carried out researches and experiments to solve the above described problems, and the present invention is proposed based on the the results of the researches and experiments. Therefore it is an object of the present invention to provide a continuously annealed blackplate for manufacturing D&I cans and deep drawn vessels, in which the contents of Ti and Mn are properly controlled, thereby ensuring a superior drawability and stable mechanical properties.
  • the continuously annealed soft temper blackplates for D&I cans and deep drawn vessels according to the present invention includes in weight %: 0.005% or less of C, 0.1 - 0.3% of Mn, 0.015% or less of S, 0.02 - 0.05% of acid soluble Al, 0.004% or less of N, 0.015 - 0.035% of Ti, and a balance of Fe and other unavoidable impurities.
  • the method for manufacturing a continuously annealed soft temper blackplate for D&I cans and deep drawn vessels includes the steps of: carrying out a hot rolling in a convertional method to an aluminum killed steel composed of in weight %: 0.005% or less of C, 0.1 - 0.3% of Mn, 0.015% or less of S, 0.02 -
  • FIG. 1 is a graphical illustration showing the variation of the amount of precipitates versus the Mn content obtained based a solubility product formula
  • FIG. 2 illustrates micrographs of EDS analysis results showing the kind and distribution of precipitates versus the Mn content
  • FIG. 3 is a graphical illustration showing the steel recrystallization completion temperature versus the contents of Mn and Ti.
  • FIG. 4 is a graphical illustration showing the planar anisotropy and the plastic anisotropy versus the reduction rate of cold rolling.
  • Carbon in the steel which acts as an interstitial solid soluble element, develops disadvantageous recrystallized texture for formability. Further, if the recrystallization temperature is to be lowered as in the case of the present invention, not only the amount of the solid soluble elements but also the formation of fine precipitates should be inhibited. Therefore, in the case where the carbon content exceeds 0.05%, carbon is bonded with Ti, with the result that fine dispersed TiC precipitates of 150 - 30 ⁇ A is increased. Further, not only the formation of a ⁇ 100 ⁇ , ⁇ 110 ⁇ texture is promoted which is disadvantageous for formability, but also the grawn growth is inhibited during the recrystallization. Therefore an undesirable result is given to the deep drawing applications.
  • nitrogen should be preferably added by 0.001% or more to prevent grainboundary embrittlement through grain boundary segregations, but this is industrially the extreme low limit, and therefore, the a specific lower limit is not specified.
  • Nitrogen is also regulated due to the same reason as the carbon, and the reason for setting the upper limit to as low as 0.004% is as follows. That is, nitrogen is an element which has an affinity with Ti, and therefore, if its amount becomes abundant, Ti is much consumed by the form of TiN. Therefore, the recrystallization temperature is raised, and the manufacturing cost is increased. That is, if nitrogen is added in a large amount, then the amount of Ti for removing sulfides and carbon becomes insufficient, and therefore, the upper limit of the nitrogen content should be preferably 0.004%.
  • Mn constitute one of the critical features of the present invention, and this feature is an improvement of the most recent invention (Korean Patent Application No. 93-29157) of the present inventors. That is, the present inventor elucidated the following fact through researches. That is, in the steel which meets the ingredients of the present invention, the Ti content is low, and therefore, the greater part of Ti is bonded with N, and the rest of Ti is bonded with S. in this procedure, a part of C is precipitated in the form of Ti-carbosulfides (TiC 2 S 2 ), with the result that a part of the solid soluble C is removed. The remaining small amount of Ti is precipitated in the form of Tie
  • the precipitating temperature of Ti sulfides and Ti-carbosulfides corresponds to the hot rolling temperature. Therefore, most of them are precipitated in the form of the strain induced precipitation and in the form of fine precipitates, and therefore, the inhibition of the grain growth is increased, with the result that the recrystallization temperature is raised.
  • Mn coworks with Ti as a scavenger of solutes in the present invention, and the precipitation is done in an early stage of the hot rolling. For this purpose, Mn is added by 0.1% or more.
  • the Mn content exceeds 0.3%, not only the manufacturing cost is increased, but also a deterioration of the mechanical properties due to the solid solution strengthening is accompanied. Therefore, its upper limit should be preferably 0.3%.
  • Aluminum is not intended to precipitate N in the form of AlN, but to remove oxygen in the steel. Therefore, in order to sufficiently remove the oxygen in molten steel, the lower limit of Al should be preferably 0.02%.
  • nitrogen is removed by Ti with a high priority, and therefore, if the Al content is too high, the manufacturing cost is increased, as well as deteriorating the temper grade and the formability of blackplates. Therefore, the upper limit of the Al content should be preferably 0.05%.
  • the Ti content is limited to 0.015% or more. The reason is that a minimum amount of Ti is required for precipitating the solid soluble N. If the Ti content exceeds 0.035%, not only N and S but also C are precipitated, with the result that the segregating C lacks in grainboundary, thereby occuring the grainboundary embrittlement of blackplates.
  • the effects of Ti content on the recrystallization and mechanical properties of blackplates were investigated, and based on the result of the study, the upper limit of the Ti content is decided to be 0.035%.
  • the steel (steel ingot) which meets the above described composition range is hot-rolled and coiled in the usual manner. Under this condition, the hot coiling temperature should be preferably 600 - 700°C. The reason for selecting this temperature range is for obtaining a proper formability and a proper surface quality.
  • the hot rolled steel sheet is cold-rolled to the target thickness with a reduction rate of 88 - 92%. This is for minimizing the formation of ears which are formed during the drawing of tinplates or tin free steel sheets.
  • the cold rolled steel sheet thus obtained is subjected to a continuous annealing, and in order to attain to the target hardness, the temperature of the continuous annealing should be preferably from recrystallization temperature to 730°C or below. The reason is that if the annealing temperature is too high, the target hardness cannot be obtained, and the mistracking, buckling and breakage of passing strip will easily occur in the continuous annealing furnace. Further, the manufacturing cost is increased, but at the above mentioned temperature, a sufficient temper grades could be obtained.
  • the continuously annealed coil is subjected to the usual temper rolling, and the elongation rate of the temper rolling should be preferably above 0.4%. The reason is that the yield point elongation phenomenon of blackplates is eliminated.
  • the continuously annealed soft temper blackplates of T2.5 or less were manuactured by present method, which has a superior drawability having an r value of 1.7 or more, a ⁇ r value of 0.2 or less and an elongation rate of 40% or more. Therefore the soft temper blackplates are very suitable for manufacturing D&I cans and deep drawn vessels.
  • the inventive steels a and b have the compositions range of the present invention, while the comparative steels 1 - 4 are extremely low carbon steel or Ti-added extremely low carbon steels in which Ti and Mn do not meet the composition range of the present invention.
  • the comparative steel 4 meets the composition range of the present inventor's conventional method (Korean Patent Application 93-29157).
  • the comparative steel 5 meets the composition range of the conventional method for manufacturing a black plate having a temper grade of T2 (Japanese Patent Laid-open No. Sho-63-33522, 61-26724, 61-16323 and 56-3413, and Hei-2-301519 ) .
  • the steels having the above described compositions were hot-rolled at a hot rolling starting temperature of 1050°C and at a hot rolling finish temperature of 910°C, and were hot-coiled at a temperature of 650°C. Then they were cold-rolled, continuously annealed and then temper rolled at the conditions set forth in Table 2 below. The mechanical properties of them were measured, and the results are shown in Table 2 below.
  • TP Temper rolling reduction ratio (%).
  • inventive steels a and b the inventive materials A-D showed a superior formability of an r value of 1.8 or more, an elongation of 40% or more and ⁇ r value of 0.2 or less at a temperature of 700°C or over. Further they showed a HR30T of 51-52 so as to satisfy a temper grade of T1-T2.5, thereby making it possible to manufacture a soft temper blackplate by a continuous annealing.
  • the inventive steels a and b were used, if they departed from the ranges of the present invention (the comparative materials E and F), the ⁇ r value became more than 0.2, the ear height of drawn can was increased, or the flange part of deep drawn vessels became irregular, so that drawability or press formability is not to be satisfied.
  • the comparative material G showed that the hardness was about 53.4 in HR30T scale, the temper grade reached the upper limit Tl (46-52), the r value was as low as 1.5, and the amount of the solute carbon in annealed blackplates was large. Therefore, with the temper rolling reduction rate of about 0.5%, the prevention of yield point elongation became insufficient, and thus the yield strength was very high. Meanwhile, in the case of comparative steel 2 having a Ti content of 0.014%, the comparative material H came within the target ranges of the present invention in various mechanical properties, but the solute carbon was not sufficiently reduced, and therefore, the r value was somewhat too low, result in insufficient formability.
  • the comparative material I showed that the recrystallization was not complete at a temperature of 730°C due to the excessive content of Ti and finely dispersed Ti precipitates. Therefore, the material was too hard, and the elongation was too low.
  • the comparative steel 4 having an MN content of 0.07% the comparative material J showed that the recrystallization became insufficient at an annealing temperature of 730°C due to the grain growth inhibition by the fine precipitates such as (Ti, Mn) S. Therefore the material properties were not good enough to use deep drawn vessels.
  • the comparative material K showed that the amount of solute carbon was very large even if the continuous annealing was carried out at a temperature higher than the usual level. Therefore, the control could not be effectively carried out, with the result that the target formability and the target temper grades could not be attained.
  • the target properties and the target temper grades can be ensured, but in this case, buckling, mistracking and breakage of strip can occur in continuous annealing line as described above.
  • the inventive steel b and the comparative steel 4 were selected from among the steels of Table 1. Then by utilizing the method of solubility products, the precipitating rates of the precipitates such as sulfides were calculated, and the results are shown in FIG. 1.
  • FIG. IA illustrates precipitation behavior of the comparative steel 4 in which the Mn content is 0.071%
  • FIG. IB illustrates the precipitation behavior of the inventive steel b in which the Mn content is 0.22%.
  • the precipitating rates were calculated in the following manner. That is, the precipitating rates of the precipitates were calculated based on the method of least squares through a basic program. Those which were simultaneously precipitated at the same temperature had a order of a precipitating, and therefore, if some kinds of precipitates have a high priority, they will be precipitated at the first and then the next ones could be precipitated. That is, such an algorithm was used.
  • the temperature is in Kelvin degrees
  • [ ] of Log is weight % of the alloying elements
  • the entries within ( ) are references. They all satisfy the formula in the austenitic region.
  • TiC* of Formula 6 indicates not the solubility product formula of the austenitic region but the solubility product formula of the ferritic region.
  • the inventive steel b showed that was precipitated at a high temperature compared with the comparative steel 4.
  • the MnS begins to precipitate during hot rolling in the comparative steel 4, so the fine MnS or (Ti,Mn)S tends to precipitate due to the strain induced precipitation.
  • the MnS precipitating temperature rose, and the amount of the precipitates before the hot rolling was increased, with the result that relatively coarse Mn-sulfides were produced.
  • the inventive steel b and the comparative steel 4 were selected. Then hot rollings were carried out at a hot rolling starting temperature of 1050°C and at a finishing temperature of 910°C. Then they were coiled at a temperature of 650°C, and then, the precipitates were observed with a transmission electron microscope(TEM) by the carbon replica method. The results are shown in FIG. 2.
  • FIG. 2A is a result of TEM observation for the inventive steel b
  • FIG. 2B is a result of that for the comparative steel 4.
  • FIG. 2C illustrates the EDS analysis results for the fine precipitates of FIG. 2A at a high magnification ratio.
  • FIG. 2D 2C illustrates the EDS analysis results for the fine precipitates of FIG 2B at a high magnification ratio.
  • the inventive steel b produced a large amount of relatively coarse precipitates, while the comparative steel 4 produced a large amount of fine " precipitates.
  • Example 4 The steels of Table 1 of Example 1 were hot-rolled at the same conditions as those of Example 3, and then, they were pickled. Then they were cold-rolled with a reduction ratio of 90%, and were subjected to continuous annealings for 30 seconds within a continuous annealing furnace of FIG. 3. Then the completely recrystallized temperatures of steels were obtained by measuring the hardness (Rockwell 30T) and by inspecting the micro-structure. The results are shown in FIG. 3 for the amounts of Mn and Ti.
  • FIG. 3A illustrates the effect of Mn content on the completely recrystallized temperature.
  • FIG. 3B illustrates the variation of compeletely recrystallized temperature versus the Ti content.
  • the recrystallization temperature of the comparative steel 1 is 610°C, while in the case of the comparative steel 3 in which 0.036% of Ti was contained, the temperature was 730°C.
  • the recrystallization temperature was lower than that of the comparative steel 4 in which the Ti content was similar. As described above, this is due to the following reasons. That is, it is due to the effect of Mn precipitates, and therefore, a proper amount of Mn is needed. Based on the above described facts, the present invention decided that the upper limit of the Ti content is 0.035%, and the lower limit of the Mn content is 0.1%. Further, the upper limit of Mn was decided to be 0.3%, because, if it is contained more in steel, the recrystallization temperature does not raise anymore, but the steel is hardened too high, and the manufacturing cost is increased.
  • the inventive steels a and b were selected from among the steels of Example 1, and then, they were hot-rolled. Then the hot rolled steel sheets were cold-rolled with a reduction ratio of 85-92%. Then they were subjected to continuous annealings at 700°C, and were subjected to temper rolled with a reduction ratio of 0.4%. Then the planar anisotropy and the plastic anisotropy of blackplates were measured, and the results are shown in FIG. 4.
  • FIG. 4A illustrates the values of planar anisotropy
  • FIG. 4B illustrates the values of plastic anisotropy.
  • the extremely low carbon steel is used, but the time point of the precipitation of fine precipitates which are usually precipitated during the hot rolling is controlled to immediately before the hot rolling.
  • the recrystallization temperature is very low, and the deviation of mechanical properties are small in continuous annealed blackplates, with the result that the product quality becomes stable.
  • the temperature of the continuous annealing is low, and therefore, there do not appear the buckling, the sheet mistracking and breakage of passing strip which usually occur during a high temperature continuous annealing.
  • solute S is precipitated and removed by Mn with a higher priority than that of Ti, and therefore, a larger amount of C can be precipitated and removed with a minimum amount of Ti compared with the conventional method. Therefore, there can be obtained a continuously annealed soft temper blackplates in which the formability is more improved than conventional technology.

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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)

Abstract

L'invention concerne un fer noir doux obtenu par recuisson en continu et laminage (T 1 à T 2,5) pour la fabrication par emboutissage et étirage/emboutissage profond de récipients tels que des bouteilles de gaz pour le camping, des boîtiers pour des piles sèches, et similaire. L'invention concerne également des procédés pour fabriquer ce fer. Ce fer contient du Ti et du Mn en quantités appropriées, pour améliorer l'aptitude à l'étirage et la stabilité du matériau. Le fer noir doux obtenu par recuisson et laminage, destiné à la fabrication de récipients par emboutissage et étirage/emboutissage profond selon la présente invention contient en % en poids: 0,005 % ou moins de C, 0,1 - 0,3 % de Mn, 0,015 % ou moins de S, 0,02 - 0,05 % d'Al acido-soluble, 0,004 % ou moins de N, 0,015 - 0,035 % de Ti, le restant étant du Fe et d'autres impuretés inévitables.
PCT/KR1996/000260 1995-12-29 1996-12-28 Fer noir doux obtenu par recuisson en continu et laminage, pour la fabrication de recipients par emboutissage et etirage/emboutissage profond WO1997024465A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP9524236A JPH10505882A (ja) 1995-12-29 1996-12-28 引抜き・アイヨニング缶および深絞り容器用連続焼鈍・軟質焼戻し黒板とその製造方法
DE19681270T DE19681270T1 (de) 1995-12-29 1996-12-28 Kontinuierlich geglühtes, weich getempertes Schwarzblech für gezogene und gestreckte Blechdosen und tiefgezogene Behälter sowie Herstellungsverfahren dafür

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1019950066239A KR970043163A (ko) 1995-12-29 1995-12-29 드로잉 및 아이어닝 캔 및 심가공용기용 연속소둔 표면처리 원판의 제조방법
KR1995/66239 1995-12-29

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WO1997024465A1 true WO1997024465A1 (fr) 1997-07-10

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PCT/KR1996/000260 WO1997024465A1 (fr) 1995-12-29 1996-12-28 Fer noir doux obtenu par recuisson en continu et laminage, pour la fabrication de recipients par emboutissage et etirage/emboutissage profond

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JP (1) JPH10505882A (fr)
KR (1) KR970043163A (fr)
CN (1) CN1066777C (fr)
DE (1) DE19681270T1 (fr)
TW (1) TW330861B (fr)
WO (1) WO1997024465A1 (fr)

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CN103350107A (zh) * 2006-12-18 2013-10-16 杰富意钢铁株式会社 钢带的表面光轧方法和高强度冷轧钢板的制造方法

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KR100570893B1 (ko) * 2001-12-17 2006-04-12 주식회사 포스코 스틸 2피스 고압캔용 고강도 석도원판의 제조방법
CN100473740C (zh) * 2005-06-29 2009-04-01 宝山钢铁股份有限公司 硬度hr30t在51±3内的软质镀锡板及其制造方法
CN100473741C (zh) * 2005-06-29 2009-04-01 宝山钢铁股份有限公司 软质镀锡板及其制造方法

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EP0171197A2 (fr) * 1984-07-09 1986-02-12 Nippon Steel Corporation Procédé de fabrication comprenant un recuit continu de tôles noires et douces pour un traitement superficiel

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EP0073092A1 (fr) * 1981-08-13 1983-03-02 Kawasaki Steel Corporation Procédé de fabrication de tôle noire à grade de dureté T-3
EP0171197A2 (fr) * 1984-07-09 1986-02-12 Nippon Steel Corporation Procédé de fabrication comprenant un recuit continu de tôles noires et douces pour un traitement superficiel

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CHEMICAL ABSTRACTS, Vol. 117, No. 8, 24 August 1992, (Columbus, Ohio, USA), page 240, Abstract No. 73687y, KUGUMINATO, HIDEO et al., "Advanced Manufacturing Process for Tin Mill Blackplates With all Temper Designations by Continuous Annealing"; & KAWASAKI SEITETSU GIHO, 1991 (Pub. 1992), 23(4), 308-14 (Japan). *

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103350107A (zh) * 2006-12-18 2013-10-16 杰富意钢铁株式会社 钢带的表面光轧方法和高强度冷轧钢板的制造方法
CN103350107B (zh) * 2006-12-18 2016-06-08 杰富意钢铁株式会社 钢带的表面光轧方法和高强度冷轧钢板的制造方法

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TW330861B (en) 1998-05-01
DE19681270T1 (de) 1998-03-19
CN1176667A (zh) 1998-03-18
KR970043163A (ko) 1997-07-26
JPH10505882A (ja) 1998-06-09

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