EP1156125B1 - Rostfreier austenitischer Stahl mit ausgezeichneter Stanzbarkeit - Google Patents

Rostfreier austenitischer Stahl mit ausgezeichneter Stanzbarkeit Download PDF

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Publication number
EP1156125B1
EP1156125B1 EP01110998A EP01110998A EP1156125B1 EP 1156125 B1 EP1156125 B1 EP 1156125B1 EP 01110998 A EP01110998 A EP 01110998A EP 01110998 A EP01110998 A EP 01110998A EP 1156125 B1 EP1156125 B1 EP 1156125B1
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European Patent Office
Prior art keywords
mass
ratio
blanking
stainless steel
plane
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Expired - Lifetime
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EP01110998A
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English (en)
French (fr)
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EP1156125A3 (de
EP1156125A2 (de
Inventor
Satoshi c/o Nisshin Steel Co. Ltd. Suzuki
Hiroshi c/o Nisshin Steel Co. Ltd. Fujimoto
Takashi c/o Nisshin Steel Co. Ltd. Igawa
Naoto c/o Nisshin Steel Co. Ltd. Hiramatsu
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Nippon Steel Nisshin Co Ltd
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Nisshin Steel Co Ltd
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Publication of EP1156125A3 publication Critical patent/EP1156125A3/de
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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

Definitions

  • the present invention relates to a method of manufacturing an austenitic stainless steel excellent in blankability, especially fine blankability.
  • Shear process, especially blanking, with a press has been applied to various kinds of metal sheets such as common steel, stainless steel and nonferrous metal, since the metal sheets can be efficiently sized to an objective shape.
  • metal sheets such as common steel, stainless steel and nonferrous metal
  • a plane formed by blanking is rugged with poor dimensional accuracy, a metal sheet is likely to be drooped at its broader surface, and thickness of the metal sheet is reduced at a part near the blanking plane.
  • a blanking plane is ground by post-treatment such as barrel finishing.
  • post-treatment is basically extra process and causes poor productivity.
  • a fine blanking method has been adopted for manufacturing a product with high dimensional accuracy.
  • clearance is determined at a very small value to suppress formation of a fracture plane, and inflow of metal is suppressed to reduce generation of drooping during blanking.
  • stainless steel has been used so far for use exposed to a corrosive or high-temperature atmosphere.
  • SUS304 is representative stainless steel suitable for such use.
  • SUS 304 austenitic stainless steel is hard material, so a life of fine blanking dies is shortened. Hardness of SUS 304 austenitic stainless steel also causes increase of a ratio of a fracture plane, which degrades quality of a blanking plane, as well as increase of drooping. Even if a shear plane is formed with high dimensional accuracy by blanking, a working cost is higher compared with a cost for blanking common steel. Accounting these disadvantages, SUS 304 austenitic stainless steel is blanked by a usual method and then ground for manufacturing a product which shall have a blanking plane with high dimensional accuracy.
  • US-patent 5,571,343 discloses an austenitic stainless steel and a respective manufacturing process, wherein the Md 30 temperature is in the range of -10 to +15.
  • JP-A-08-109447 discloses an austenitic stainless steel with high press formability and corrosion resistance.
  • JP-A-10-121207 discloses an austenitic stainless steel which is excellent in workability after punching.
  • EP-A-0 594 866 discloses a Cr-Ni stainless steel sheet produced by strip castling.
  • the present invention aims at provision of an austenitic stainless steel, in which softening and stability of an austenite phase are controlled so as to increase a ratio of a shear plane, especially suitable for fine blanking.
  • the present invention proposes a method of manufacturing an austenitic stainless steel having an excellent property in fine blankability, said method comprising the steps of:
  • the inventors have researched from various aspects on the relationship of material properties of austenitic stainless steel with a state of a blanking plane formed by fine blanking, and discovered that a ratio of a strain-induced martensite ( ⁇ ' phase) puts a significant influence on a ratio of a shear plane to a blanking plane.
  • the strain-induced martensite ( ⁇ ' phase) is harder and inferior of ductility, compared with an austenitic ( ⁇ phase) matrix. Excessive generation of the strain-induced martensite ( ⁇ ' phase) means degradation of ductility, early occurrence of fracture at a blanking plane and decrease of a ratio of shear plane. If generation of the strain-induced martensite ( ⁇ ' phase) is too little on the contrary, the austenitic stainless steel is blanked as such in the ⁇ phase inferior of ductility, resulting in early occurrence of fracture at a blanking plane and decrease of a ratio of shear plane.
  • the austenitic stainless steel of the method of the present invention contains various alloying components at predetermined ratios as follows: (C+1/2N) up to 0.060 mass %
  • C and N are components effective for adjusting stability of an austenite phase.
  • excessive addition of C and N makes the austenite phase harder due to solution-hardening, and also makes a strain-induced martensite phase harder.
  • the hardening causes increase of blanking load and short life of dies. Therefore, a ratio of (C+1/2N) is controlled at 0.060 mass % or less. Si up to 1.0 mass %
  • Si is an alloying component added as a deoxidizing agent at a steel refining step. Excessive addition of Si makes an austenite phase harder due to solution-hardening, and degrades blankability of the stainless steel. In this regard, an upper limit of Si content is determined at 1.0 mass %. Mn up to 5 mass %
  • Mn is an alloying component effective for stabilizing the austenite phase and improving blankability of the stainless steel. These effects become apparent as increase of Mn content. But, excessive addition of Mn more than 5 mass % causes increase of nonmetallic inclusions which put harmful influences on corrosion resistance and workability. S up to 0.006 mass %
  • Ni is an alloying element for stabilizing the austenite phase. Such an effect is realized by addition of Ni at a ratio of 5 mass % or more. Blankability of the stainless steel is also improved as increase of Ni content. However, Ni is an expensive element and raises a steel cost, so that an upper limit of Ni content is determined at 12 mass %.. Cu up to 5 mass %
  • Cu is an alloying element effective for improvement of blankability and also stabilization of the austenite phase.
  • Mo 0-3.0 mass %
  • Mo is an optional alloying element effective for improvement of corrosion resistance. But, excessive addition of Mo more than 3.0 mass % makes the stainless steel too hard resulting in degradation of fine blankability.
  • a value Md 30 (representing a ratio of a strain-induced martensite): -60 to -10
  • the ratio of hardness increase is defined by the formula of (Vickers hardness of a cold-rolled steel sheet)-(Vickers hardness of an annealed steel sheet)] / (Vickers hardness of an annealed steel sheet) x 100 (%) in this specification.
  • the ratio of hardness increase of 20% or more is necessary to suppress occurrence of drooping caused by blanking to a half or less of drooping which is generated by blanking an as-annealed steel sheet.
  • an extremely hardened steel sheet causes increase of shear resistance during blanking and promotes abrasion of dies.
  • an upper limit of the ratio of hardness increase is preferably determined at 150%, accounting the effect on reduction of drooping in balance with die life.
  • Each annealed steel sheet was examined by the under-mentioned blanking test to research shear resistance, a ratio of a shear plane to a blanking plane and a ratio of droop to thickness, and its Vickers hardness was measured as Rockwell B hardness regulated at JIS Z2240.
  • Each disc (a blanked piece) was measured with a laser-type noncontacting position sensor at 8 points, i.e. every 2 points along a rolling direction, a crosswise direction and a direction inclined with 45 degrees with respect to the rolling direction as shown in Fig. 1, to detect a degree of droop Z at each point.
  • the measured values were averaged, and a ratio of droop to thickness was calculated as a ratio of the mean value to thickness of the test piece.
  • Thickness of a shear plane S of each disc was also measured at 8 points, i.e. every 2 points along a rolling direction, a crosswise direction and a direction inclined with 45 degrees with respect to the rolling direction, as shown in Fig. 2.
  • the measured values were averaged, and a ratio of a shear plane was calculated as a ratio of the mean value to thickness of the test piece.
  • Sample Nos. 1-3 and 13-16 which had values Md 30 within a range of -60 to -10 and contained (C+1/2N) less than 0.06 mass %, were blanked with a clearance ratio of 2%.
  • a ratio of a shear plane formed by the blanking was researched in relationship with S content of each Sample. Results are shown in Fig. 5. It is noted that Sample Nos. 1-3, 13 and 14 containing S less than 0.006 mass % were blanked with a ratio of a shear plane being 100%, while Sample Nos. 15 and 16 containing S more than 0.006 mass % were blanked with ratios of a shear plane being 95% and 71%, respectively.
  • the relationship of S content with a ratio of a shear plane is also varied in response to a clearance ratio even in case of blanking the same steel sheet. That is, when Sample Nos. 13 and 14 were blanked with a clearance ratio of 2%, a blanking plane was formed with a ratio of a shear plane being 100%. The ratio of a shear plane was reduced to 92% and 88%, respectively, when Sample Nos. 13 and 14 were blanked with a clearance ratio of 5%, as shown in Fig. 6. The results prove that controlling S content less than 0.003 mass % is effective for blanking the steel sheet with a big clearance ratio which causes reduction of a ratio of a shear plane.
  • FIG. 7 shows a relationship of Vickers hardness of each test piece with a ratio of a shear plane. It is noted that any of annealed or temper-rolled Sample Nos. A1 to A6 was blanked with a ratio of a shear plane being 100%. On the other hand, Sample Nos. B1 to B3 corresponding to SUS304 were blanked with low ratios of a shear plane near 45%.
  • a shear droop ratio was calculated as (a ratio of droop to thickness in a temper-rolled steel sheet) / (a ratio of droop to thickness in an annealed steel sheet), to research an effect of hardness increase by temper-rolling on generation of drooping. Results are shown in Fig. 8. It is noted that a shear droop ratio of any temper-rolled steel sheet A3 to A6 hardened by 20% or more as Vickers hardness was less than 50%, i.e. less than a half of droop generated in the annealed steel sheet A1.
  • a shear droop ratio of the temper-rolled steel sheet A2 hardened at a ratio of hardness increase less than 20% was about 70% compared with the annealed steel sheet A1. The results prove that hardness increase of 20% or more is effective for sufficient reduction of drooping.
  • Stainless steels C, D having compositions shown in Table 4 were melted, cast and hot-rolled to thickness of 10mm at an initial temperature. Thereafter, each hot-rolled steel sheet was annealed 1 minute at 1150°C, pickled with an acid, cold-rolled to thickness of 5 mm, annealed 1 minute at 800-1100°C, and then pickled again with an acid.
  • a shear droop ratio with a grain size number is illustrated in Fig. 10.
  • the relationship proves improvement of a shear droop ratio as increase of a grain size number (i.e. minimized metallurgical structure) regardless kinds of steel sheets.
  • a shear droop ratio of any steel sheet C3 to C6 each having grain size number more than #8 is reduced to a half or less, compared with steel sheets C1, C2 of grain size number less than #8.
  • An austenitic stainless steel maunfactured by the method of the present invention can be blanked to a product with high dimensional accuracy, due to excellent blankability, especially fine blankability. Even when the steel sheet is blanked with a small clearance ratio, a ratio of a shear plane to a blanking plane can be kept at a higher level without occurrence of substantial drooping.
  • the stainless steel sheet is also advantageous for elongation of die life, compared with conventional austenitic stainless steel sheets such as SUS304. Consequently, blanked products with high dimensional accuracy are obtained from the austenitic stainless steel sheet without increase of a manufacturing cost.

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

Claims (1)

  1. Verfahren zur Herstellung eines austenitischen rostfreien Stahls mit einer ausgezeichneten Eigenschaft in der Feinstanzbarkeit, wobei das Verfahren die Schritte umfaßt:
    das Bereitstellen einer Stahlzusammensetzung, bestehend aus (C+1/2N) bis zu 0,060 Masse-%, Si bis zu 1,0 Masse-%, Mn bis zu 5 Masse-%, S bis zu 0,006 Masse-%, 15-20 Masse-% Cr, 5-12 Masse-% Ni, Cu bis zu 5 Masse-%, gegebenenfalls Mo bis zu 3,0 Masse-%, wobei der Rest Fe mit Ausnahme unvermeidlicher Verunreinigungen ist, mit der Maßgabe, daß ein Wert Md30, der ein Verhältnis einer Spannungs-induzierten Martensitphase, definiert durch die folgende Formel, darstellt, innerhalb eines Bereichs von -60 bis -10 ist; das herkömmliche Heißwalzen, Glühen und Beizen der Stahlzusammensetzung;
    das Kaltwalzen des Stahlblechs, um so dessen gewalzte Struktur 1,2 mal härter in der Vickers-Härte als dessen derart geglühte Struktur zu machen; und
    das Fertigglühen des kaltgewalzten Stahlblechs, um so dessen metallurgische Struktur auf #8 bis #10 in der Korngrößenzahl, reguliert unter JIS G0551, zu minimieren.
    Md30=551-462(C+N)-9,2Si-29(Ni+Cu)-8,1 Mn-13,7Cr-18,5Mo
EP01110998A 2000-05-16 2001-05-07 Rostfreier austenitischer Stahl mit ausgezeichneter Stanzbarkeit Expired - Lifetime EP1156125B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2000142644 2000-05-16
JP2000142644A JP3691341B2 (ja) 2000-05-16 2000-05-16 精密打抜き性に優れたオーステナイト系ステンレス鋼板

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EP1156125A2 EP1156125A2 (de) 2001-11-21
EP1156125A3 EP1156125A3 (de) 2002-01-30
EP1156125B1 true EP1156125B1 (de) 2006-08-30

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US (1) US20020015655A1 (de)
EP (1) EP1156125B1 (de)
JP (1) JP3691341B2 (de)
KR (1) KR100421511B1 (de)
CN (1) CN1145713C (de)
DE (1) DE60122618T2 (de)
ES (1) ES2270918T3 (de)
MY (1) MY146900A (de)
SG (1) SG108254A1 (de)
TW (1) TW500811B (de)

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KR101964314B1 (ko) * 2017-08-21 2019-08-07 주식회사포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
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EP1156125A3 (de) 2002-01-30
ES2270918T3 (es) 2007-04-16
CN1327078A (zh) 2001-12-19
EP1156125A2 (de) 2001-11-21
MY146900A (en) 2012-10-15
TW500811B (en) 2002-09-01
DE60122618T2 (de) 2007-09-27
SG108254A1 (en) 2005-01-28
US20020015655A1 (en) 2002-02-07
KR100421511B1 (ko) 2004-03-09
JP2001323342A (ja) 2001-11-22
JP3691341B2 (ja) 2005-09-07
DE60122618D1 (de) 2006-10-12
CN1145713C (zh) 2004-04-14
KR20010105193A (ko) 2001-11-28

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