EP0889145B1 - Rostfreier austenoferritischer Stahl mit sehr niedrigem Nickelgehalt und hoher Zugverformung - Google Patents

Rostfreier austenoferritischer Stahl mit sehr niedrigem Nickelgehalt und hoher Zugverformung Download PDF

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Publication number
EP0889145B1
EP0889145B1 EP98401308A EP98401308A EP0889145B1 EP 0889145 B1 EP0889145 B1 EP 0889145B1 EP 98401308 A EP98401308 A EP 98401308A EP 98401308 A EP98401308 A EP 98401308A EP 0889145 B1 EP0889145 B1 EP 0889145B1
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steel
content
austenite
steels
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EP98401308A
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English (en)
French (fr)
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EP0889145A1 (de
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Jean-Michel Hauser
Hervé Sassoulas
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Ugitech SA
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Ugine SA
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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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/51—Plural diverse manufacturing apparatus including means for metal shaping or assembling
    • Y10T29/5183—Welding strip ends
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12958—Next to Fe-base component
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12958—Next to Fe-base component
    • Y10T428/12965—Both containing 0.01-1.7% carbon [i.e., steel]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
    • Y10T428/12979—Containing more than 10% nonferrous elements [e.g., high alloy, stainless]

Definitions

  • Stainless steels are classified by major families in function of their metallurgical structures, after treatment thermal.
  • This last family includes steels which are generally rich in chromium and nickel, i.e. they have respective chromium and nickel contents greater than 20% and more than 4%.
  • the structure of these steels, after treatment at a temperature between 950 ° C and 1150 ° C consists of ferrite and austenite in proportion generally greater than 30% for either of the two phases.
  • austenoferritic steels concerns welding properties. After a welding operation, the structure of these stainless steels, in the molten zone and in the zone affected by the heat remains strongly polyphase in ferrite and austenite, unlike austenitic steels whose weld remains mainly austenitic. This results in characteristics high mechanical welds, desired characteristics when welded assemblies have to withstand stresses mechanical operating.
  • certain finely austenitic austenoferritic steels divided can have a high plasticity called superplasticity during slow hot forming.
  • austenoferritic steels also exhibit disadvantages, such as their high price due to their composition with a high nickel content or due to manufacturing difficulties, in particular linked to their high content of chromium such as, for example, the formation of a weakening sigma phase or demixing into an iron-rich ferrite and a chromium-rich ferrite with weakening of the steels during cooling after rolling to hot.
  • the object of the invention is the development of a steel austenoferritic containing in its composition a very low content nickel and having the advantageous characteristics of the family austenoferritic associated with general characteristics improved.
  • FR-A-2 119 612 discloses an austenoferritic stainless steel having good ductility and comprising, in% by weight, 0.008% C, 0.42% Si, 3.36% Mn, 0.20% Ni, 20.57% Cr, 0.007% S, 0.006% P, 0.22% N, rest: iron and impurities.
  • the single figure presents a curve showing the dependence of the elongation characteristic with the IM index.
  • the invention relates to an austenoferritic steel containing reduced alloying elements and in particular a content of nickel less than 1% and a chromium content less than 22%.
  • the low nickel content is imposed, for economic and ecological, the reduction of the chromium content allowing a on the one hand, to ensure an easy production of steel and on the other hand, to avoid hot embrittlement both during the production of said steel when in use.
  • the invention is the result of research following which found that a specific area of composition allows on the family of steel considered, obtaining a particular improvement in tensile elongation associated with a high elastic limit.
  • Steel can be produced as molded products or forged, hot or cold rolled sheet, bars, tubes or of sons.
  • Table 2 below presents the characteristics of steels in the area of the IM index and the equivalent chromium / equivalent nickel ratio.
  • D VS B AT AT (bottom S) E F VS (bottom S) VS VS (bottom S, B) IM 144 81 78 35 38 51 68 78 12 85 Creq / Nieq 2.92 2.57 2.74 2.51 2.61 2.50 2.39 2.55 2.41 2.64
  • steel is subjected to a forging from the temperature of 1200 ° C then to a transformation hot from 1240 ° C to obtain, for example, a laminated strip 2.2 mm thick.
  • the strip is treated at 1050 ° C. then soaked in water.
  • the hot rolled strip can then be cold rolled and again treated at 1040 ° C for one minute and then quenched with water.
  • steels presented are composed of ferrite and austenite with the exception of steel D which also contains martensite formed during the cooling of austenite.
  • the structure steel is always free of carbides and nitrides.
  • B and C only C low S, B according to the invention
  • F have on the one hand, a elongation at break greater than or equal to 40% when they are developed with the long range, and on the other hand, elastic limits greater than 450 MPa as well as higher breaking loads at 700 MPa.
  • steel C (only C low S, B according to the invention) has both an elastic limit high and particularly high elongation.
  • Table 4 below presents the mechanical characteristics for steels B and C (only C low S, B according to the invention), subject to the two preparation ranges, for steels E and F according to the invention, subject to the long range of preparation, characteristics compared to those of steels A and D.
  • Mechanical characteristics Steel Elastic limit Rp0.2% (Mpa) limit at break Rm (Mpa) elongation.
  • steels B, C and F whose IM index is respectively 78, 81 and 68, that is to say between 40 and 115, have a particularly high elongation compared to steels A and D.
  • Table 5 presents the rate of martensite hardening formation under the effect of traction on steels subjected to hyper quenching at 1040 ° C.
  • steels B and C respectively, 12% and 52% of the initial austenite are transformed into martensite during traction, which gives them good ductility; on the contrary, steel A does not shows no transformation of austenite into martensite during the tensile and steel D has an austenite transformation rate, 74% too high, which gives it insufficient ductility.
  • Tables 6 and 7 show traction characteristics hot from different steels.
  • the mechanical properties were evaluated on an annealed wrought steel. The working is done by forging from 1200 ° C. The steel is then annealed at a temperature of 1100 ° C for 30 min.
  • the tensile specimens used are specimens having a barrel of circular section with a diameter of 8 mm and a length of 5 mm. They are subjected to a preheating of 5 min at 1200 ° C or 1280 ° C, then to a cooling of 2 ° C / s until the test temperature at which the traction is carried out, traction carried out at the speed of 73 mm / s.
  • the high hot ductility characteristics are obtained according to the invention in the presence of a very low sulfur content.
  • Steel C containing 35.10-4% sulfur does not have a sufficient hot ductility.
  • the carbon content cannot exceed 0.04% otherwise chromium carbides precipitate on cooling after heat treatment at the ferrite - austenite interfaces and degrade the corrosion resistance.
  • a carbon content of less than 0.03% avoids this precipitation at cooling speeds the weaker.
  • the silicon content must necessarily be greater than 0.4% to avoid excessive oxidation when reheating slabs or blooms. It is limited to 1.2% to avoid promoting weakening precipitation of intermetallic or sigma phase during hot processing. Preferably, the silicon content is between 0.5% and 1%.
  • the manganese content cannot exceed 4% to avoid development difficulties.
  • a minimum content of 2% is however necessary to make the steel austenitic, allowing the introduction of more than 0.1% nitrogen, without exceeding the limit of nitrogen solubility on solidification.
  • the nickel content is deliberately limited to 1% for economic reasons and also to limit corrosion under voltage in chlorinated media.
  • molybdenum can optionally be carried out to improve corrosion resistance; its effectiveness does not increase hardly beyond 3%, moreover, molybdenum tends to increase the embrittlement by sigma phase formation and its addition must be limited.
  • An addition of copper is particularly effective for increase the austenite content. Beyond 4%, it appears hot rolling defects in relation to segregation of solidification rich in copper. It also makes it possible to harden the phase ferrite by heat treatment between 400 ° C and 600 ° C, and can have, during use, a bactericidal and fungicidal effect.
  • This low sulfur content can be obtained by the controlled use of calcium and aluminum to obtain the desired content ranges for Ca, Al and S.
  • a boron content of 5 to 30.10 -4 % also improves hot ductility.
  • the phosphorus content is less than 0.1% and preferably 0.04% to avoid hot cracking during welding.
  • the nitrogen content is naturally limited to 0.3% by its solubility in steel during its production.
  • the content of nitrogen should preferably be less than 0.2%.
  • a minimum of 0.1% nitrogen is required to obtain a quantity of austenite more than 30%.
  • the chromium content is low enough to avoid embrittlement due to the sigma phase and ferrite-ferrite demixing, during hot processing.
  • the chromium contents according to the invention also allow superplastic forming at temperatures moderate between 700 ° C and 1000 ° C without formation of sigma phase weakening, unlike the usual austenoferritic nuances used for superplastic forming.
  • An austenite content of 30 to 70% is required to obtain high mechanical characteristics, i.e. a limit elastic higher than 400 MPa on elaborate steel and on welding, the solder to be hard and resilient, with a rate of austenite greater than 20%.
  • the elongation in tension higher than 35% is obtained if the IM index is between 40 and 115, and the steel according to the invention has good characteristics under these conditions stamping.
  • the steel according to the invention is particularly intended for the use of stamped parts then assembled by welding such as propellant tanks or tanks containing other reagents pyrotechnics usable in particular for cushion devices automotive safety inflatables, applications requiring steel with high ductility for shaping as well as equally high yield strength of base metal and weld necessary in the use considered.
  • tubes from rolled and then welded strips, usable in particular in the construction of mechanical structures fixed or incorporated in mobile vehicles.
  • These tubes can be shaped using high pressure forming processes, called hydroforming.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Carbon And Carbon Compounds (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Metal Extraction Processes (AREA)

Claims (8)

  1. Rostfreier austenoferritischer Stahl mit sehr niedrigem Nickelgehalt und hoher Zugverformung, gekennzeichnet durch folgende gewichtsanalytische Zusammensetzung:
    Kohlenstoff < 0,04%
    0,4% < Silizium < 1,2%
    2% < Mangan < 4%
    0,1%< Nickel < 1%
    18% < Chrom < 22%
    0,05% < Kupfer < 4%
    fakultativ 0,010% - 0,030% Aluminium
    fakultativ 0,0005% - 0,0020% Kalzium
    0,0005% < Bor < 0,0030%
    Schwefel < 0,0015%
    Phosphor < 0,1%
    0,1% < Stickstoff < 0,3%
    Molybdän < 3%
    Rest: Eisen
    wobei der Stahl eine zwischen 30% und 70% Austenit liegende Zweiphasigkeit aufweist, wie Creq = Cr% + Mo% + 1,5 Si% Nieq = Ni% + 0,33 Cu% + 0,5 Mn% + 30 C% + 30 N%    wobei Creq/Nieq zwischen 2,3 und 2,75 liegt,
    die Stabilität des Austenits, des Stahls, über den IM-Index, welcher von der gewichtsanalytischen Zusammensetzung des Stahls ausgehend, eingestellt wird IM = 551 - 805(C+N)% - 8,52 Si% - 8,57 Mn% - 12,51 Cr% -36 Ni% - 34,5 Cu%
    - 14 Mo%,        wobei IM zwischen 40 und 115 liegen muß.
  2. Stahl nach Anspruch 1, dadurch gekennzeichnet, daß die Zusammensetzung folgender Beziehung genügt: Creq/Nieq liegt zwischen 2,4 und 2,65.
  3. Stahl nach den Ansprüchen 1 und 2, dadurch gekennzeichnet, daß der Kohlenstoffgehalt kleiner oder gleich 0,03% ist.
  4. Stahl nach den Ansprüchen 1 bis 3, dadurch gekennzeichnet, daß der Stickstoffgehalt zwischen 0,12% und 0,2% liegt.
  5. Stahl nach den Ansprüchen 1 bis 4, dadurch gekennzeichnet, daß der Chromgehalt zwischen 19% und 21% liegt.
  6. Stahl nach den Ansprüchen 1 bis 5, dadurch gekennzeichnet, daß der Siliziumgehalt zwischen 0,5% und 1% liegt.
  7. Stahl nach den Ansprüchen 1 bis 6, dadurch gekennzeichnet, daß der Kupfergehalt kleiner als 3% ist.
  8. Stahl nach den Ansprüchen 1 bis 7, dadurch gekennzeichnet, daß der Phosphorgehalt kleiner oder gleich 0,04% ist.
EP98401308A 1997-06-30 1998-06-02 Rostfreier austenoferritischer Stahl mit sehr niedrigem Nickelgehalt und hoher Zugverformung Expired - Lifetime EP0889145B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9708180 1997-06-30
FR9708180A FR2765243B1 (fr) 1997-06-30 1997-06-30 Acier inoxydable austenoferritique a tres bas nickel et presentant un fort allongement en traction

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EP0889145A1 EP0889145A1 (de) 1999-01-07
EP0889145B1 true EP0889145B1 (de) 2003-03-19

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US (1) US6096441A (de)
EP (1) EP0889145B1 (de)
JP (1) JPH1171643A (de)
KR (1) KR19990007429A (de)
CN (1) CN1078262C (de)
AT (1) ATE234945T1 (de)
AU (1) AU738930B2 (de)
BR (1) BR9802386A (de)
CA (1) CA2239478C (de)
DE (1) DE69812234T2 (de)
DK (1) DK0889145T3 (de)
ES (1) ES2193488T3 (de)
FR (1) FR2765243B1 (de)
ID (1) ID20517A (de)
PT (1) PT889145E (de)
TW (1) TW474997B (de)
ZA (1) ZA985176B (de)

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TW474997B (en) 2002-02-01
CN1209465A (zh) 1999-03-03
AU738930B2 (en) 2001-09-27
ZA985176B (en) 1999-01-08
DE69812234D1 (de) 2003-04-24
US6096441A (en) 2000-08-01
BR9802386A (pt) 1999-07-06
CA2239478A1 (fr) 1998-12-30
FR2765243A1 (fr) 1998-12-31
FR2765243B1 (fr) 1999-07-30
CA2239478C (fr) 2009-04-07
ATE234945T1 (de) 2003-04-15
EP0889145A1 (de) 1999-01-07
ID20517A (id) 1999-01-07
CN1078262C (zh) 2002-01-23
JPH1171643A (ja) 1999-03-16
DE69812234T2 (de) 2004-02-05
DK0889145T3 (da) 2003-07-21
PT889145E (pt) 2003-06-30
KR19990007429A (ko) 1999-01-25
AU6984598A (en) 1999-01-07

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