EP1156125A2 - Acier inoxydable austénitique avec une facilité de poinçonnage excellente - Google Patents

Acier inoxydable austénitique avec une facilité de poinçonnage excellente Download PDF

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Publication number
EP1156125A2
EP1156125A2 EP01110998A EP01110998A EP1156125A2 EP 1156125 A2 EP1156125 A2 EP 1156125A2 EP 01110998 A EP01110998 A EP 01110998A EP 01110998 A EP01110998 A EP 01110998A EP 1156125 A2 EP1156125 A2 EP 1156125A2
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EP
European Patent Office
Prior art keywords
mass
ratio
stainless steel
blanking
plane
Prior art date
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Granted
Application number
EP01110998A
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German (de)
English (en)
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EP1156125B1 (fr
EP1156125A3 (fr
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 date
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Publication of EP1156125A2 publication Critical patent/EP1156125A2/fr
Publication of EP1156125A3 publication Critical patent/EP1156125A3/fr
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Publication of EP1156125B1 publication Critical patent/EP1156125B1/fr
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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 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.
  • 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 new austenitic stainless steel having compositions consisting of (C+1/2N) up to 0.060 mass %, Si up to 1.0 mass %, Mn up to 5 mass %, S up to 0.006 mass %, 15-20 mass % Cr, 5-12mass % Ni, Cu up to 5 mass %, 0-3.0 mass % Mo and the balance being essentially Fe.
  • a value Md 30 which represents a ratio of a strain-induced martensite phase, defined by the under-mentioned formula is adjusted within a range of -60 to -10.
  • Md 30 551-462(C+N)-9.2Si-29(Ni+Cu)-8.1Mn-13.7Cr-18.5Mo
  • the austenitic stainless steel is manufactured by a conventional process involving hot-rolling, annealing, pickling, cold-rolling and finish annealing.
  • a ratio of hardness increase in a cold-rolled state is preferably controlled at a value of 20% or more as Vickers hardness.
  • the stainless steel in the finish annealed state is preferably conditioned to a metallurgical structure of grain size number (regulated in JIS G0551 ) within a range of 8-11.
  • Fig. 1 is a schematic view for explaining generation of drooping in a blanked piece and positions for detection of drooped parts.
  • Fig. 2 is a schematic view for explaining formation of a shear plane at a blanking plane of a product and positions for measuring the shear plane.
  • Fig. 3 is a graph showing a relationship of Md 30 value with a ratio of a shear plane.
  • Fig. 4 is a graph showing a relationship of (C+1/2N) with a ratio of a shear plane.
  • Fig. 5 is a graph showing a relationship of S content with a ratio of a shear plane at a clearance ratio of 2%.
  • Fig. 6 is a graph showing a relationship of S content with a ratio of a shear plane at a clearance ratio of 5%.
  • Fig. 7 is a graph showing a relationship of Vickers hardness with a ratio of a shear plane.
  • Fig. 8 is a graph showing a relationship of hardness increase caused by temper-rolling with a shear droop ratio.
  • Fig. 9 is a graph showing a relationship of a grain size number with a ratio of a shear plane.
  • Fig. 10 is a graph showing a relationship of a grain size number with a shear droop ratio.
  • 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 proposed austenitic stainless steel contains various alloying components at predetermined ratios as follows:
  • a ratio of the strain-induced martensite ( ⁇ ' phase) can be calculated from components and contents of an austenitic stainless steel.
  • the austenitic stainless steel is designed to the composition having the value Md 30 controlled within a range of -60 to -10, a ratio of a shear plane is higher as explained in under-mentioned Examples , and a blanking plane is formed with high dimensional accuracy.
  • 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 .
  • a test piece cut off each annealed steel sheet was blanked to a disc shape with clearance of 0.1mm or 0.25mm (a clearance ratio calculated as clearance/thickness of a test piece is 2% or 5%, respectively) at a blanking speed of 600 mm/minute, using a punch of 50mm in outer diameter and a die of 50.2mm or 50.5mm in inner diameter.
  • 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.
  • the ratio of a shear plane formed by blanking each test piece with a clearance ratio of 2% was researched in relationship with a value Md 30 of each test piece. Results are shown in Fig. 3 . It is noted that a blanking plane with a ratio of a shear plane being 100% was gained at a Md 30 value within a range of -60 to -10. Although Sample Nos. 4 , 15 and 16 had Md 30 values within a range of -60 to -10, their blanking planes were exceptionally poor with ratios of a shear plane being 85%, 95% and 71%, respectively.
  • Sample Nos. 1-3 and 13-16 b 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.
  • Stainless steels having compositions shown in Table 2 were melted, cast, hot-rolled to thickness of 10mm at an initial temperature of 1230°C. Thereafter, each hot-rolled steel sheet was annealed 1 minute at 1150°C, pickled with an acid, cold-rolled to intermediate thickness of 5-8mm, annealed 1 minute at 1050°C, and pickled again with an acid. Some of the steel sheets were provided as annealed steel sheets ( A1, B1 ) of 5mm in thickness. The other annealed steel sheets of intermediate thickness were further cold-rolled to thickness of 5mm and provided as temper-rolled steel sheets ( A2-A6, B2,B3 ).
  • 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 test piece was cut off each steel sheet pickled after being annealed, and blanked with a clearance ratio of 2% under the same conditions as in Example 1 .
  • a ratio of a shear plane in the blanked test piece was calculated to research its relationship with grain size number of the steel sheet. Results are shown in Fig. 9 . It is noted that any of type-C steel sheets according to the present invention was blanked with a ratio of a shear plane being 100% regardless its grain size number. On the other hand, any of type- D steel sheets corresponding to SUS304 was blanked with a lower ratio of a shear plane near 45%.
  • 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 proposed by 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 proposed 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)
EP01110998A 2000-05-16 2001-05-07 Acier inoxydable austénitique avec une facilité de poinçonnage excellente Expired - Lifetime EP1156125B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
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
JP2000142644 2000-05-16

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

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EP01110998A Expired - Lifetime EP1156125B1 (fr) 2000-05-16 2001-05-07 Acier inoxydable austénitique avec une facilité de poinçonnage excellente

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

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EP1249513A1 (fr) * 2001-04-12 2002-10-16 Nisshin Steel Co., Ltd. Feuillard d'acier inoxydable doux présentant une excellente aptitude au formage
FR2864108A1 (fr) * 2003-12-22 2005-06-24 Ugine Et Alz France Tole en acier inoxydable presentant une grande resistance et un bon allongement, et procede de fabrication
WO2006016010A1 (fr) * 2004-07-08 2006-02-16 Ugine & Alz France Composition d'acier inoxydable austenitique et son utilisation pour la fabrication de pieces de structure de moyens de transport terrestres et de containers
EP2025770A1 (fr) * 2007-08-09 2009-02-18 Nisshin Steel Co., Ltd. Acier inoxydable austénitique à teneur réduite en Ni
EP2072631A1 (fr) * 2007-12-20 2009-06-24 Ugine & Alz France Tole en acier inoxydable austenitique et procédé d'obtention de cette tole
EP3561125A4 (fr) * 2016-12-23 2019-10-30 Posco Produit traité en acier inoxydable austénitique présentant d'excellentes caractéristiques de surface et son procédé de fabrication

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KR100784888B1 (ko) * 2000-08-01 2007-12-11 닛신 세이코 가부시키가이샤 자동차용 스테인리스강 연료탱크
US20040265238A1 (en) * 2003-06-27 2004-12-30 Imtiaz Chaudry Inhalable formulations for treating pulmonary hypertension and methods of using same
US7745452B2 (en) * 2005-03-09 2010-06-29 Merck Sharp & Dohme Corp. Quinazolinone T-type calcium channel antagonists
US20100066779A1 (en) 2006-11-28 2010-03-18 Hanan Gothait Method and system for nozzle compensation in non-contact material deposition
CA2692783A1 (fr) * 2007-07-10 2009-01-15 Merck Sharp & Dohme Corp. Antagonistes de canal calcique de type t au quinazolinone
CN101994068B (zh) * 2009-08-25 2012-12-26 宝山钢铁股份有限公司 奥氏体不锈钢钢板
WO2011027847A1 (fr) * 2009-09-02 2011-03-10 新日鐵住金ステンレス株式会社 Acier inoxydable à faible teneur en ni ayant une excellente résistance à la corrosion
CN101791648A (zh) * 2010-04-10 2010-08-04 中精集团有限公司 一种不锈钢厚板的冲压工艺
KR20120132691A (ko) * 2010-04-29 2012-12-07 오또꿈뿌 오와이제이 높은 성형성을 구비하는 페라이트-오스테나이트계 스테인리스 강의 제조 및 사용 방법
KR101659186B1 (ko) * 2014-12-26 2016-09-23 주식회사 포스코 가요성이 우수한 오스테나이트계 스테인리스강
KR101964314B1 (ko) * 2017-08-21 2019-08-07 주식회사포스코 가공성 및 내시효균열성이 우수한 오스테나이트계 스테인리스강 및 이를 이용한 드로잉 가공품
CN113265585B (zh) * 2021-05-14 2023-02-24 山西太钢不锈钢股份有限公司 一种汽车安全气囊用不锈钢及其生产方法与应用

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JPH07216512A (ja) * 1994-01-31 1995-08-15 Sumitomo Metal Ind Ltd 耐応力腐食割れ性、深絞り性に優れたオーステナイトステンレス鋼
JPH08120419A (ja) * 1994-08-31 1996-05-14 Nisshin Steel Co Ltd 温間絞り成形用または温間・常温絞り成形用オーステナイト系ステンレス鋼板およびその温間絞り成形法
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JPH10121207A (ja) * 1996-10-14 1998-05-12 Nisshin Steel Co Ltd 打抜き後の加工性に優れたオーステナイト系ステンレス鋼
JPH10130784A (ja) * 1996-10-23 1998-05-19 Sanyo Special Steel Co Ltd 耐塩酸性及び冷間加工性に優れたセミオーステナイト型析出硬化ステンレス鋼

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PATENT ABSTRACTS OF JAPAN vol. 012, no. 186 (C-500), 31 May 1988 (1988-05-31) & JP 62 290829 A (NISSHIN STEEL CO LTD), 17 December 1987 (1987-12-17) *
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 10, 30 November 1995 (1995-11-30) & JP 07 180000 A (NKK CORP), 18 July 1995 (1995-07-18) *
PATENT ABSTRACTS OF JAPAN vol. 1995, no. 11, 26 December 1995 (1995-12-26) & JP 07 216512 A (SUMITOMO METAL IND LTD), 15 August 1995 (1995-08-15) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 08, 30 August 1996 (1996-08-30) & JP 08 109447 A (NIKKO KINZOKU KK), 30 April 1996 (1996-04-30) *
PATENT ABSTRACTS OF JAPAN vol. 1996, no. 09, 30 September 1996 (1996-09-30) & JP 08 120419 A (NISSHIN STEEL CO LTD), 14 May 1996 (1996-05-14) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 10, 31 August 1998 (1998-08-31) & JP 10 121207 A (NISSHIN STEEL CO LTD), 12 May 1998 (1998-05-12) *
PATENT ABSTRACTS OF JAPAN vol. 1998, no. 10, 31 August 1998 (1998-08-31) & JP 10 130784 A (SANYO SPECIAL STEEL CO LTD), 19 May 1998 (1998-05-19) *

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1249513A1 (fr) * 2001-04-12 2002-10-16 Nisshin Steel Co., Ltd. Feuillard d'acier inoxydable doux présentant une excellente aptitude au formage
FR2864108A1 (fr) * 2003-12-22 2005-06-24 Ugine Et Alz France Tole en acier inoxydable presentant une grande resistance et un bon allongement, et procede de fabrication
WO2006016010A1 (fr) * 2004-07-08 2006-02-16 Ugine & Alz France Composition d'acier inoxydable austenitique et son utilisation pour la fabrication de pieces de structure de moyens de transport terrestres et de containers
EP2025770A1 (fr) * 2007-08-09 2009-02-18 Nisshin Steel Co., Ltd. Acier inoxydable austénitique à teneur réduite en Ni
EP2072631A1 (fr) * 2007-12-20 2009-06-24 Ugine & Alz France Tole en acier inoxydable austenitique et procédé d'obtention de cette tole
EP3561125A4 (fr) * 2016-12-23 2019-10-30 Posco Produit traité en acier inoxydable austénitique présentant d'excellentes caractéristiques de surface et son procédé de fabrication
US11299799B2 (en) 2016-12-23 2022-04-12 Posco Austenitic stainless steel product having excellent surface properties and manufacturing method of the same

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ES2270918T3 (es) 2007-04-16
US20020015655A1 (en) 2002-02-07
KR100421511B1 (ko) 2004-03-09
DE60122618T2 (de) 2007-09-27
KR20010105193A (ko) 2001-11-28
EP1156125B1 (fr) 2006-08-30
CN1327078A (zh) 2001-12-19
CN1145713C (zh) 2004-04-14
TW500811B (en) 2002-09-01
JP2001323342A (ja) 2001-11-22
EP1156125A3 (fr) 2002-01-30
JP3691341B2 (ja) 2005-09-07
DE60122618D1 (de) 2006-10-12
SG108254A1 (en) 2005-01-28
MY146900A (en) 2012-10-15

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