WO1990000454A1 - PROCEDE DE FABRICATION DE TOLES MINCES EN ACIER INOXYDABLE Cr-Ni, DE QUALITE ET FINITION EXCELLENTES - Google Patents

PROCEDE DE FABRICATION DE TOLES MINCES EN ACIER INOXYDABLE Cr-Ni, DE QUALITE ET FINITION EXCELLENTES Download PDF

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Publication number
WO1990000454A1
WO1990000454A1 PCT/JP1989/000692 JP8900692W WO9000454A1 WO 1990000454 A1 WO1990000454 A1 WO 1990000454A1 JP 8900692 W JP8900692 W JP 8900692W WO 9000454 A1 WO9000454 A1 WO 9000454A1
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WO
WIPO (PCT)
Prior art keywords
cooling
steel
less
solidification
grains
Prior art date
Application number
PCT/JP1989/000692
Other languages
English (en)
Japanese (ja)
Inventor
Masanori Ueda
Shinichi Teraoka
Hidehiko Sumitomo
Toshiyuki Suehiro
Masayuki Abe
Shigeru Minamino
Original Assignee
Nippon Steel Corporation
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP22147188A external-priority patent/JPH0730406B2/ja
Priority claimed from JP63221472A external-priority patent/JPH0730407B2/ja
Priority to KR1019900700496A priority Critical patent/KR930000089B1/ko
Application filed by Nippon Steel Corporation filed Critical Nippon Steel Corporation
Priority to DE68925578T priority patent/DE68925578T3/de
Priority to EP89908266A priority patent/EP0378705B2/fr
Publication of WO1990000454A1 publication Critical patent/WO1990000454A1/fr
Priority to KR1019900700496A priority patent/KR900701434A/ko

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • 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

Definitions

  • the present invention produces a C r -N i type stainless steel thin plate with a mirror piece thickness close to the product thickness by a so-called synchronous continuous ironing process with no relative velocity difference between the hook piece and the inner wall of the iron mold.
  • the present invention relates to a method for producing a Cr-Ni-based stainless steel thin plate having excellent surface properties by refining the structure from the mirror piece stage.
  • the steel mold was vibrated in the steelmaking direction, and the steel pieces with a thickness of 100 thighs or more were steelworked, and the surface of the obtained longevity piece was cared for. After heating to 1000'C or higher in a heating furnace, hot rolling is performed with a hot strip mill consisting of a row of rough rolling mills and finishing rolling mills. It was up.
  • the papers featured in '85, A197-'85, and A256 disclose the process of directly obtaining hot strips by the discontinuous manufacturing.
  • we are trying to obtain the streaks (strips)! The twin drum method is also used when the level is 1 to 10 mm)! : When the level is 20 to 50 IM, the twin belt method is considered / ⁇
  • These new steelmaking machines, which have no relative speed difference between the stall and the inner wall of the stylus, are so-called synchronous continuous mirrors. It is called a manufacturing process.
  • a strip (strip) with a thickness equal to or close to that of the hot strip is obtained by continuous manufacturing.
  • the surface properties of stainless steel products are sensitively affected by the characteristics of the flake, because the process from the manufacturing process to the product is simplified. That is, in order to obtain a product having excellent surface properties, it is necessary to obtain excellent pieces of life.
  • an object of the present invention to provide an excellent tin plate capable of obtaining a product having an excellent surface texture and material in a continuous steelmaking process of a stainless steel iron piece having a melting point of 10 or less.
  • the present invention is a simple and powerful way to obtain a Cr-Ni-based stainless steel sheet without surface unevenness called gloss unevenness and mouth-bing phenomenon, which is peculiar to a stainless steel sheet product manufactured by a thin continuous steelmaking device.
  • the purpose is to provide a simple manufacturing process.
  • the inventors have succeeded in controlling the surface defects of the product by controlling the cooling of the steel plate directly under the steelmaking in the high temperature range (temperature range of 1 100 ⁇ or more).
  • the roving generated on the surface of the product is prevented, and by controlling the cooling in the low temperature range (900 to 550'C temperature range), the luster is improved.
  • the inventors of the present invention found that if the particle size is 50 sq. Or less, it has a significant effect on the prevention of ⁇ -bing formation.
  • the present invention was completed by developing quenching means, cold rolling means, hot rolling means, and the like.
  • One of the features of the present invention is the cooling of the Cr-Ni type stainless steel typified by 18% Cr-8% Ni steel when it is solidified by a continuous steelmaking machine in which the steel wall moves in synchronization with the steel pieces. Continuous strip forming with a speed of lOiTCZsec or more on thin strips with a thickness of 10 thighs or less-.
  • Another feature is to provide a manufacturing method in which hot rolling, cold rolling, or annealing is added to the cooling control means.
  • the present inventors first conducted the following tests in order to know the surface properties of products.
  • Molten steel containing SUS 304 steel as a basic component is manufactured by an internal water-cooled twin-gall continuous tubing tester into a thin strip with a thickness of 2 to 4 mm and cooled. I took it off.
  • the tin pieces (thin seaweed) thus obtained were descaled, directly cold-rolled, finally annealed and pickled to obtain 2 ⁇ products.
  • This The surface texture of these products was obtained by heating a conventional piece of armor with a thickness of 100 sq. Or more, hot rolling it with a hot strip mill, and then cold rolling it.
  • molten steel was produced by an internal water-cooled twin roll (Twin Drum) continuous steel making tester to form thin strips with a thickness of 2-4. It was found that the following surface defects may occur in the cold rolled, final annealed, pickled and 2B product.
  • Uneven luster occurs due to sensitization of the structure of the material during winding, grain boundary oxidation or coarsening of r grain.
  • a thin steel piece that is, a steel piece having a thickness of 10 mm or less is produced at a cooling rate of 100'CZsec or more by a continuous iron making machine such as a twin roll method or a single roll method. If the thickness of the slab exceeds 10 liters, it will be difficult to make r-grains finer, and it will be difficult to manufacture them by the direct cold rolling method.
  • Cooling is started from as high temperature as possible directly below, and cooling is performed by increasing the average cooling rate in the r-grain growth temperature range up to 1100 to 100'C Zsec or higher as much as possible to suppress r-grain growth. To do.
  • Creq becomes complicated in these intermediate regions due to the addition of the peritectic eutectic reaction, but a component system that causes ⁇ solidification is advantageous for suppressing the growth of ⁇ grains.
  • the combination of component selection that delays the onset of ⁇ precipitation by utilizing solidification and rapid cooling of the high temperature region is effective for controlling the growth of r grains and making them finer.
  • ⁇ -Fe.cal (%) 3 (Cr + 1.5 S i + Mo + Nb + T i) — 2.8
  • Fig. 2 (a), (b), (c) shows the metallographic micrographs of ⁇ ? 1 Fe.cai
  • the above basic technique is extremely effective for refining r grains, but it is effective to add the following means to reduce the average grain size of r grains to the following. .. That is,
  • Figure 1 shows the cross-sectional state diagram of the portion corresponding to Creq + Nieq 30% in the ternary equilibrium diagram of the Fe-Cr-Ni system.
  • Figures 2 (a), (b), and (c) show the set of (2) -thick slabs made by continuously forming molten steels with different composition of (? -Pe.cal (%)).
  • Figure 3 shows the relationship between strain load and cracking just below the melting point of SUS 304 steel
  • Fig. 4 is a diagram showing the temperature-time relationship of the ribbon when the Cr-Ni series stainless steel ribbon is produced by twin-roll (water cooling) continuous mirroring machine,
  • Figure 5 shows the rolling reduction of hot rolled steel with llOiTC at ⁇ -Fe.cal (%) of about 1%, and the rolling reduction ratio after hot rolling with llOiTC. Diagram showing the effect of the rolling reduction when rolling on the roving height of the product surface,
  • Figure 6 shows the process of the present invention after pre-cold rolling (cold working) of a strip (thin strip) under the application of various reduction ratios.
  • Diagram showing the relationship between the rolling reduction when performing cold rolling (final cold rolling) to the final thickening after recrystallization by annealing at 1080 ° C for a short time and the mouth-pit height on the product surface Is.
  • the size of the r-grain of the beak pieces is reduced by reducing the r-grain during solidification and suppressing the subsequent growth of the r-grain. In order to do so, it is important to cool from a high temperature.
  • case (3) is the case where the material is air-cooled after manufacturing, and the material is rapidly cooled by the ironing machine in the iron making machine, but when it leaves the ironing machine, it reheats and the temperature rises. Cooling is slower than the case of cooling from just below the ram, and if it is wound as it is, r grains grow during cooling after winding, resulting in cavities and C.r carbide folding. Sensitization due to exposure, etc .. Problems with surface characteristics such as uneven light occur.
  • case (1) is a case where hot rolling is performed after steelmaking to cause recrystallization of the mirror piece to make r grains finer, and after hot rolling, the sensitization of Cr carbide is prevented by spilling. It shows the process of rapid cooling.
  • case (2) in order to promote finer granulation of the slab from case (1), quenching is performed after steelmaking and then hot working is performed. R grain after smelting is better than that in case (1). Since it becomes fine, very fine r-grains can be obtained when hot rolling is applied, and after hot rolling, a quenching process is shown to prevent sensitization due to cracking of Cr carbide. ..
  • Figure 5 shows that the hot rolling reduction when hot rolling at 1100'C was carried out on the strips cooled at 5 — Fe.cal (%) of about 1% was the roping height of the cold rolled sheet. The effect is shown.
  • the effect of hot rolling is remarkable, and the rolling reduction is 20% or more to reach the level of the scale, and the higher it is to 30% or more, the lower the rolling height of the product becomes, and the "waviness" on the surface is recognized. Recrystallization is observed inside the slabs at a reduction of 20% or more in hot rolling, and almost entirely at about 30%.
  • the average particle size of-r grains was less than 50 s.
  • one Fe.cal (%) is set to about 3%, and the steel pieces are cooled directly under the twin rolls (cooling drum), and the temperature difference between the surface diagram of the steel pieces and the inside of the steel pieces is given to make the hot work.
  • good ⁇ -bing characteristics were obtained even when the rolling reduction was about 10%.
  • Quantity and Roll (cooling drum) It can be seen that the effect of cooling the chips directly below the roll is great.
  • Hot rolling is carried out in the region where the surface temperature of the slab is over 900 ° C and promotes the recrystallization inside the slab.
  • the inside of the strip is in a high temperature region (within 10 seconds after the strip is made)
  • the effect is saturated even when a rolling reduction of more than 60% is applied.
  • the temperature difference between the surface layer and the inside of the slab becomes small, and the refining effect of r grains is diminished.
  • Hot-rolled sheet is baked at a temperature of 950 ° C or higher to allow recrystallization to proceed.
  • the temperature and time are controlled and annealing is performed so that the average r grain size does not exceed 50 s.
  • the ⁇ -F decreased during annealing, which was smaller than that of the flake stage. Since it can be slower than the cooling of the hot-rolled sheet, the cooling rate of the Cr carbide protrusion area was set to 10'C / "s or more.
  • the roasted piece thus obtained is subjected to preliminary cold working, for example, cold rolling, and then annealed at high temperature for a short time. And the crystal is recrystallized.
  • Figure 6 shows that the steel strip was pre-cold-rolled, and then annealed for 1080'C for a short time, and then cold-rolled to the final thickness (main cold-rolling).
  • the relationship between the rolling reduction and the height of the flat bing in the product is shown according to the rolling reduction level in the preliminary cold rolling.
  • the r-grain of the slab is fine, for example, when a thin slab, such as two thighs, is continuously produced, and cooling of the slab is 100'C in the temperature range of 1300 to: L 100 directly under the steelmaking machine.
  • the strength is higher than / sec, even if the reduction ratio in pre-cooled mining rolling is as low as 10% or more, II crystal is sufficiently formed, and the average ⁇ grain size can be refined to 50 sq. or less. The height of one bing can be lowered.
  • the higher the cooling rate of 1300 to 110 (TC in the temperature range of 1300 to 110 (TC'C), the higher the cooling rate of 100'C Zsec, the lower the draft of pre-cold working (rolling, etc.). It is possible to crystallize even if it is low, and it is possible to make the average ⁇ grain size after recrystallization as small as 50 sq. Or less, which makes it possible to reduce the roving of the product and is excellent in gloss and even surface quality. You can get the product.
  • composition of the composition of the thin pieces of iron, 5 — Feca (%) is controlled to be in the range of — 2% to: L0%, it is possible to easily refine the r grain in parallel with the rapid cooling in the high temperature range. ..
  • the effects of the present invention will be further specifically shown by Examples.
  • a cooling means by means of an internal cooling type roll was placed to cool the slabs and prevent reheat to cool them. Some misting cooling means were also placed after the roll cooling.
  • the average cooling rate from 1200 to 400 is 220 to 56, although it depends on the thickness of the plate and the speed at which it is built. As cooled. After that, in the range of 900 to 550 ° C, it was cooled by water cooling at a cooling rate of 5 (TC / sec or more and wound up.
  • ⁇ -Fe.cai (%) 3 (Cr + 1.5S i + Mo + Nb + T i) —
  • the tin pieces were hot rolled within a temperature range of 1100 to 950 within 8 seconds after the steel was formed.
  • the rolling reduction at this time was between about 10% and 50% (Table 4).
  • the strip was cooled at a cooling rate of 60 / s or more between 900 and 550 ° C, and was wound at 600 or less.
  • Comparative materials include those without hot rolling and those with a cooling rate of 10 ° C / sec or less after annealing of the hot rolled sheet.
  • the material was pickled, descaled, cold-rolled, and then annealed or bright annealed normally.
  • the surface properties of the products thus obtained were investigated. Particular attention was paid to the roving height and gloss of the product surface. As shown in Table 4, in the examples shown in this example, the ⁇ grains were finely divided due to the effect of hot rolling, and the subsequent cooling was sufficient. The surface texture was shown.
  • the steel pieces were descaled by mechanical descaling and pickling, and pre-cold rolled by cold rolling. Both 3 thigh and 4.5 thigh pieces were pre-cold rolled in the range of 10-40%, annealed at 1000'C or more for 20 seconds and then rapidly cooled. Thus, the silver flakes were recrystallized and the r particle size was reduced to 50 sq.
  • molten iron of the same composition was manufactured by the twin-drum method, and cooling up to 1100 was less than 100'C Zsec, and further cooling up to 550'C was 70 and cooling in Zsec.
  • the product is wound up between 650 and 600'C, then descaled and cold-rolled into a product, the surface texture is improved by increasing the cold rolling reduction. Was left inadequate.
  • the present invention is configured and operated as described above, it is a simple process for directly obtaining a thin strip having a thickness close to the product thickness by the continuous manufacturing method, and the surface quality is It is possible to obtain a Cr-Ni series stainless steel thin plate with excellent material.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Procédé de fabrication d'une pièce coulée mince sous forme d'une tôle d'acier inoxydable Cr-Ni ayant sensiblement la même épaisseur que celle d'un produit final, par coulage en continu synchronisé, procédé comprenant: la trempe à haute température de la pièce immédiatement après coulage, la transformation à chaud ou à froid de ladite pièce, le recuit, etc. destinés à réduire la taille des grains gamma et le refroidissement à une température plus basse, égale ou inférieure à 900°C, afin d'empêcher la précipitation de carbure de chrome à la limite des grains. Ce procédé permet de réduire la tendance au vrillage ou l'irrégularité du brillant sur la surface de la tôle en acier inoxydable.
PCT/JP1989/000692 1988-07-08 1989-07-10 PROCEDE DE FABRICATION DE TOLES MINCES EN ACIER INOXYDABLE Cr-Ni, DE QUALITE ET FINITION EXCELLENTES WO1990000454A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
KR1019900700496A KR930000089B1 (ko) 1988-07-08 1989-07-08 표면품질과 재질이 우수한 Cr-Ni계 스테인레스강 시이트의 제조방법
DE68925578T DE68925578T3 (de) 1988-07-08 1989-07-10 Verfahren zur herstellung dünner bleche aus cr-ni und rostfreiem stahl mit ausgezeichneten eigenschaften, sowie oberflächenqualität und materialqualität
EP89908266A EP0378705B2 (fr) 1988-07-08 1989-07-10 PROCEDE DE FABRICATION DE TOLES MINCES EN ACIER INOXYDABLE Cr-Ni, DE QUALITE ET FINITION EXCELLENTES
KR1019900700496A KR900701434A (ko) 1988-07-08 1990-03-08 표면품질과 재질이 우수한 Cr-Ni계 스테인레스강 시이트의 제조방법

Applications Claiming Priority (7)

Application Number Priority Date Filing Date Title
JP63/169095 1988-07-08
JP16909488 1988-07-08
JP19409688 1988-08-03
JP63/221471 1988-09-06
JP22147188A JPH0730406B2 (ja) 1988-07-08 1988-09-06 表面品質と材質が優れたＣｒ−Ｎｉ系ステンレス薄鋼板の製造法
JP63/221472 1988-09-06
JP63221472A JPH0730407B2 (ja) 1988-07-08 1988-09-06 表面品質が優れたＣｒ―Ｎｉ系ステンレス鋼薄板の製造方法

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WO1990000454A1 true WO1990000454A1 (fr) 1990-01-25

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0449289A2 (fr) * 1990-03-30 1991-10-02 Nippon Steel Corporation Procédé de fabrication d'alliages de système Fe-Ni ayant une grande perméabilité
AU644672B2 (en) * 1990-08-13 1993-12-16 Thyssen Edelstahlwerke Ag Method and device for manufacturing a semi-ferritic stainless steel strip from molten metal

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61189845A (ja) * 1985-02-18 1986-08-23 Nippon Kokan Kk <Nkk> 薄板状鋳片の製造方法
JPS62197247A (ja) * 1986-02-21 1987-08-31 Nippon Yakin Kogyo Co Ltd 異方性が小さくかつ結晶粒が粗大化し難いオーステナイト系ステンレス鋼薄板帯の製造方法
JPS63421A (ja) * 1986-06-19 1988-01-05 Nippon Steel Corp 表面特性と材質のすぐれたオ−ステナイト系ステンレス鋼薄板の新製造法
JPS63216924A (ja) * 1987-03-03 1988-09-09 Nippon Steel Corp 発銹抵抗が大きく研磨性にすぐれたＣｒ−Ｎｉ系ステンレス鋼の製造法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61189845A (ja) * 1985-02-18 1986-08-23 Nippon Kokan Kk <Nkk> 薄板状鋳片の製造方法
JPS62197247A (ja) * 1986-02-21 1987-08-31 Nippon Yakin Kogyo Co Ltd 異方性が小さくかつ結晶粒が粗大化し難いオーステナイト系ステンレス鋼薄板帯の製造方法
JPS63421A (ja) * 1986-06-19 1988-01-05 Nippon Steel Corp 表面特性と材質のすぐれたオ−ステナイト系ステンレス鋼薄板の新製造法
JPS63216924A (ja) * 1987-03-03 1988-09-09 Nippon Steel Corp 発銹抵抗が大きく研磨性にすぐれたＣｒ−Ｎｉ系ステンレス鋼の製造法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP0378705A4 *

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0449289A2 (fr) * 1990-03-30 1991-10-02 Nippon Steel Corporation Procédé de fabrication d'alliages de système Fe-Ni ayant une grande perméabilité
EP0449289A3 (en) * 1990-03-30 1992-12-02 Nippon Steel Corporation Method of manufacturing high permeability fe-ni system alloy
AU644672B2 (en) * 1990-08-13 1993-12-16 Thyssen Edelstahlwerke Ag Method and device for manufacturing a semi-ferritic stainless steel strip from molten metal

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