EP2072631A1 - Tole en acier inoxydable austenitique et procédé d'obtention de cette tole - Google Patents

Tole en acier inoxydable austenitique et procédé d'obtention de cette tole Download PDF

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Publication number
EP2072631A1
EP2072631A1 EP07291575A EP07291575A EP2072631A1 EP 2072631 A1 EP2072631 A1 EP 2072631A1 EP 07291575 A EP07291575 A EP 07291575A EP 07291575 A EP07291575 A EP 07291575A EP 2072631 A1 EP2072631 A1 EP 2072631A1
Authority
EP
European Patent Office
Prior art keywords
sheet
steel
hot
temperature
stainless steel
Prior art date
Legal status (The legal status 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 status listed.)
Withdrawn
Application number
EP07291575A
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German (de)
English (en)
French (fr)
Inventor
Thomas Frohlich
Jean-Denis Mithieux
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Aperam Stainless France SA
Original Assignee
Ugine et Alz France SA
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
Application filed by Ugine et Alz France SA filed Critical Ugine et Alz France SA
Priority to EP07291575A priority Critical patent/EP2072631A1/fr
Priority to SI200832034T priority patent/SI2245203T1/sl
Priority to PT08872296T priority patent/PT2245203T/pt
Priority to PL08872296T priority patent/PL2245203T3/pl
Priority to PCT/FR2008/001687 priority patent/WO2009101285A1/fr
Priority to ES08872296T priority patent/ES2708578T3/es
Priority to EP08872296.2A priority patent/EP2245203B1/fr
Priority to HUE08872296A priority patent/HUE042000T2/hu
Priority to TR2019/00950T priority patent/TR201900950T4/tr
Priority to DK08872296.2T priority patent/DK2245203T3/en
Publication of EP2072631A1 publication Critical patent/EP2072631A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for drawing, e.g. for deep-drawing
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • 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

Definitions

  • the invention relates to stainless steel sheets having high mechanical properties and good resistance to corrosion in order to be intended in particular for the manufacture of automotive parts, such as structural parts or engine head gaskets.
  • the stainless steels considered here are in the sense given to this expression by the ISO 6929 standard, ie steels containing at least 10.5% by weight of chromium and not more than 1 , 2% by weight of carbon.
  • austenitic steels are alloy steels containing chromium, nickel, manganese, nitrogen, carbon and optionally copper and molybdenum, in order to produce an austenitic microstructure, which has the advantage of presenting a large crystalline mesh for the iron (cubic face-centered), which increases the solubility of the various elements of alloys in iron, including carbon.
  • the usual process for producing austenitic stainless steels is as follows: after hot rolling of a strip followed by annealing, a cold rolling is carried out whose rate depends on the final characteristics concerned. The steel then has good mechanical strength, but its ductility is too low, especially for its subsequent shaping. To overcome this, it is subjected to a final recrystallization treatment in the form of an annealing furnace, that is to say a heating with temperature maintenance the time required for complete recrystallization before controlled cooling.
  • the main objective of an annealing is, remember, to put the metal in a structural state close to the state of stable thermodynamic equilibrium. In short, the internal energy accumulated during the cold-working is evacuated.
  • a recrystallization annealing will use this internal energy differential to promote the germination of new metal grains and their growth. It is understood that the greater the internal energy increase due to hardening is important, the more likely there will be new seeds during the annealing, and thus a small final grain size. Also, is it advantageous to perform a strong work hardening prior to annealing.
  • the recrystallization temperature is also an important parameter for controlling the final grain size since the mobility of the grain boundaries increases with temperature. It is therefore recommended to lower the annealing temperature to obtain a fine grained structure.
  • the heating conventionally used during the recrystallization annealing is also a quenching, ie it must exceed the solvus of the chromium carbides to put in solution all the carbon in the austenite.
  • the objective of this step is to avoid any risk of localized corrosion caused by decrepit areas around chromium carbides.
  • the solution temperature of the chromium carbides thus constitutes a limit to the decrease of the annealing temperature in order to refine the microstructure. This limit depends on the chemical composition and mainly the carbon content.
  • said heat treatment is a total recrystallization annealing comprising a rapid heating phase, at a speed V C of between 50 and 800 ° C./s up to a temperature of between T C and T C + 50 ° C. C, T C designating the total recrystallization temperature, followed by cooling at a speed V R greater than 50 ° C / s.
  • the rapid heating is up to a temperature between 800 and 900 ° C.
  • the heat treatment is a partial recrystallization annealing comprising rapid heating phase at a speed V C between 50 and 800 ° C / s down to a temperature between T c and T c -50 ° C , T C designating the total recrystallization temperature, followed by cooling at a speed V R greater than 50 ° C / s.
  • the rapid heating is up to a temperature between 700 and 800 ° C.
  • the heat treatment further comprises a destabilization phase of the structure, this phase consisting of cooling the sheet at a speed greater than 50 ° C./s up to a temperature of approximately 750 ° C and maintain it for a holding time of between 1 and 100s to obtain a precipitation of chromium carbides.
  • the cooled sheet is subjected to a cold deformation operation capable of generating the appearance of martensite.
  • the rapid heating is preferably carried out by electromagnetic induction.
  • the resistance may vary between about 1000 and 1600 MPa.
  • the invention also relates to an installation for implementing a recrystallization annealing comprising an electromagnetic induction heating device for rapidly heating the sheet during the heating phase during the implementation of the method defined above. .
  • the invention essentially consists of a new sheet of austenitic stainless steel with very fine grains, having a significant carbon content, greater than 0.05 or 0.09%, and in a new process for obtaining a sheet from this steel which offsets the undesired effects of this increase in the carbon content by a very rapid heating annealing to quickly reach the recrystallization temperature.
  • the main problem raised by the recrystallization annealing of austenitic stainless steel is that it can proceed to recrystallization without the precipitation of chromium carbides.
  • these carbides are detrimental to the corrosion resistance of the steel, but they also prevent the recrystallization from starting.
  • the nose of the precipitation zone of these carbides will shift to the left: the domain A 1 is relative to steels with steels less than 0.05% C, the domain A 2 to steels with higher carbon content. Carbides will form more easily and therefore faster.
  • One solution would be to heat the steel at temperatures beyond that zone and hold it there until the carbides recoat. Unfortunately, the temperatures to achieve to achieve this are such that the time elapsed and the mobility of the grain boundaries do not allow then to obtain a fine grain.
  • the present inventors have discovered that it is possible to obtain a homogeneous and complete recrystallization or quenching of the steel before the chromium carbides precipitate, and this for carbon contents of up to at 0.3%, or even a little beyond.
  • the maximum allowable carbon contents to obtain recrystallization and avoid precipitation of the carbides would be around 0.07 to 0, 08% on average. A maximum of 0,15% C even could have been reached sometimes by certain nuances.
  • the balance of the composition consists of iron and other elements usually expected to be found as impurities resulting from the processing of stainless steel, in proportions that do not affect the properties sought.
  • the slab is hot rolled in a strip train to form a hot rolled sheet. This is annealed at a temperature above 1000 ° C in order to allow subsequent cold rolling. The sheet is then etched by a method known per se.
  • the hot rolled sheet is then cold rolled at room temperature at a reduction rate of greater than 40%.
  • This rolling will generate many dislocations within the steel. It will even form martensite (called martensite deformation) which is in the form of slats. These microstructural evolutions will increase the internal energy of steel. The increase in temperature during treatment thermal process that will follow, will allow to bring the metal back to thermodynamic equilibrium.
  • the heat treatment according to the invention consists in subjecting the cold-rolled steel sheet to a recrystallization annealing comprising, in a first step, a rapid heating phase, at a speed of between 50 and 800 ° C./s. to reach a temperature between T C and T C + 50 ° C. Fast heating is preferably carried out at 800 to 900 ° C.
  • This temperature must be reached before the onset of precipitation of chromium carbides. After cooling under the conditions according to the invention, an ultra-fine austenitic grain having an average size of less than 2 microns is obtained.
  • obtaining a fine grain does not only depend on the rate of preliminary hardening, but also the annealing conditions (temperature and hold time).
  • the higher the carbon content of the steel the higher the heating rate must be.
  • the heating rate should reach about 100 ° C / s.
  • such a heating rate is achieved by the use of an electromagnetic induction heating device.
  • an electromagnetic induction heating device Proper implementation of such a device, in particular by the choice of the frequency of the electric excitation current, makes it possible to obtain temperatures so high that it is no longer even necessary to provide a maintenance phase of homogenization as can be seen on the figure 2 .
  • an advantage of the process according to the invention is that there is less loss of internal energy during the heating phase. It therefore becomes possible to obtain the same fineness of grain for a lower work hardening rate than in the past.
  • the steel is then cooled to ambient temperature at a cooling rate V R greater than 50 ° C / sec. In this way a fine microstructure is obtained without chromium carbides precipitated on cooling.
  • Another embodiment presented to the figure 3 consists in cooling the sheet in stages.
  • a first cooling is performed at a speed greater than 50 ° C / s, so as to be placed in the vicinity of the precipitation nose under isothermal conditions.
  • This first cooling is carried out, for example, up to the temperature of about 750 ° C., where a maintenance lasting from 1 to 100 seconds is carried out.
  • the sheet is cooled to room temperature.
  • the chromium carbides will predominantly precipitate, that is to say for more than 90% of them, at the austenitic grain boundaries.
  • This precipitation after austenitization will destabilize the structure and increase the final mechanical characteristics of the steel. Indeed, chromium carbides predominantly precipitating at austenitic grain boundaries, and the latter being very fine, there is less risk at this level to deteriorate the resistance to intergranular corrosion.
  • the invention will be particularly useful for the manufacture of motor cylinder head gaskets, which require a high yield strength and good resistance to fatigue and corrosion.

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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)
  • Gasket Seals (AREA)
EP07291575A 2007-12-20 2007-12-20 Tole en acier inoxydable austenitique et procédé d'obtention de cette tole Withdrawn EP2072631A1 (fr)

Priority Applications (10)

Application Number Priority Date Filing Date Title
EP07291575A EP2072631A1 (fr) 2007-12-20 2007-12-20 Tole en acier inoxydable austenitique et procédé d'obtention de cette tole
SI200832034T SI2245203T1 (sl) 2007-12-20 2008-12-03 Avstenitna nerjavna jeklena pločevina in postopek za izdelavo te pločevine
PT08872296T PT2245203T (pt) 2007-12-20 2008-12-03 Chapa em aço inoxidável austenítico e método para a obtenção dessa chapa
PL08872296T PL2245203T3 (pl) 2007-12-20 2008-12-03 Blacha z nierdzewnej stali austenitycznej i sposób otrzymywania tej blachy
PCT/FR2008/001687 WO2009101285A1 (fr) 2007-12-20 2008-12-03 Tôle en acier inoxydable austenitique et procede d'obtention de cette tôle
ES08872296T ES2708578T3 (es) 2007-12-20 2008-12-03 Lámina de acero inoxidable austetínico y procedimiento de obtención de esta lámina
EP08872296.2A EP2245203B1 (fr) 2007-12-20 2008-12-03 Tôle en acier inoxydable austenitique et procede d'obtention de cette tôle
HUE08872296A HUE042000T2 (hu) 2007-12-20 2008-12-03 Ausztenites rozsdamentes acéllemez és eljárás annak elõállítására
TR2019/00950T TR201900950T4 (tr) 2007-12-20 2008-12-03 Östenitli paslanmaz çelikten levha ve bu levhanın elde edilmesine yönelik yöntem.
DK08872296.2T DK2245203T3 (en) 2007-12-20 2008-12-03 Stainless austenitic steel plate and process for making this plate

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP07291575A EP2072631A1 (fr) 2007-12-20 2007-12-20 Tole en acier inoxydable austenitique et procédé d'obtention de cette tole

Publications (1)

Publication Number Publication Date
EP2072631A1 true EP2072631A1 (fr) 2009-06-24

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EP07291575A Withdrawn EP2072631A1 (fr) 2007-12-20 2007-12-20 Tole en acier inoxydable austenitique et procédé d'obtention de cette tole
EP08872296.2A Active EP2245203B1 (fr) 2007-12-20 2008-12-03 Tôle en acier inoxydable austenitique et procede d'obtention de cette tôle

Family Applications After (1)

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EP08872296.2A Active EP2245203B1 (fr) 2007-12-20 2008-12-03 Tôle en acier inoxydable austenitique et procede d'obtention de cette tôle

Country Status (9)

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EP (2) EP2072631A1 (pl)
DK (1) DK2245203T3 (pl)
ES (1) ES2708578T3 (pl)
HU (1) HUE042000T2 (pl)
PL (1) PL2245203T3 (pl)
PT (1) PT2245203T (pl)
SI (1) SI2245203T1 (pl)
TR (1) TR201900950T4 (pl)
WO (1) WO2009101285A1 (pl)

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013107922A1 (en) * 2012-01-20 2013-07-25 Jl Materials Technology Oy An austenitic stainless steel product and a method for manufacturing same
CN103484779A (zh) * 2013-09-05 2014-01-01 常熟市勤丰铸件厂 一种不锈钢铸件
CN106011681A (zh) * 2016-06-27 2016-10-12 武汉科技大学 一种提高316ln奥氏体不锈钢力学性能的方法
CN111727269A (zh) * 2018-03-15 2020-09-29 日铁不锈钢株式会社 马氏体系不锈钢板及其制造方法以及弹簧构件
CN113637924A (zh) * 2020-04-27 2021-11-12 靖江市中信特种机械泵阀厂 一种醪液泵新型材料
CN114480977A (zh) * 2021-12-13 2022-05-13 四川大学 一种低温2500MPa级超高强高韧钢及其制备方法
CN115595420A (zh) * 2022-12-13 2023-01-13 太原科技大学（Cn） 一种高强韧含铜不锈钢及其生产工艺
CN118241037A (zh) * 2024-05-29 2024-06-25 太原科技大学 一种具有双峰组织的含铜不锈钢及其制备方法

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CN106906428B (zh) * 2015-12-23 2020-07-14 宝钢德盛不锈钢有限公司 一种传送带用硬态奥氏体不锈钢及其制造方法和应用
KR102292016B1 (ko) 2019-11-18 2021-08-23 한국과학기술원 균일하게 분포하는 나노 크기의 석출물을 다량 함유한 오스테나이트계 스테인리스강 및 이의 제조방법
CN113667903B (zh) * 2021-08-11 2022-05-06 浙江久立特材科技股份有限公司 一种阶梯组织奥氏体不锈钢、无缝管及其制备方法和应用
CN113957322A (zh) * 2021-10-29 2022-01-21 烟台汽车工程职业学院 一种提高301不锈钢变形过程中马氏体形核能力及含量的方法
CN114317904B (zh) * 2022-01-05 2024-01-19 无锡派克新材料科技股份有限公司 一种航空发动机用沉淀硬化高温合金锻件成型方法
CN115948694B (zh) * 2022-11-07 2023-07-14 鞍钢股份有限公司 一种45mm以下高性能奥氏体不锈钢板及其制造方法
CN115927965A (zh) * 2022-12-16 2023-04-07 广东甬金金属科技有限公司 一种铁镍合金及其应用以及一种焊接胀形强塑性铁镍不锈钢带及其制备方法
CN118653098B (zh) * 2024-08-22 2024-12-17 鞍钢股份有限公司 一种储氢容器用奥氏体不锈钢板及其制造方法

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US10329649B2 (en) * 2012-01-20 2019-06-25 Solu Stainless Oy Austenitic stainless steel product and a method for manufacturing same
WO2013107922A1 (en) * 2012-01-20 2013-07-25 Jl Materials Technology Oy An austenitic stainless steel product and a method for manufacturing same
US20140338800A1 (en) * 2012-01-20 2014-11-20 Jl Materials Technology Oy Austenitic stainless steel product and a method for manufacturing same
CN104379773A (zh) * 2012-01-20 2015-02-25 Jl材料工艺有限公司 奥氏体不锈钢产品及其制造方法
CN104379773B (zh) * 2012-01-20 2017-09-12 索罗不锈有限责任公司 奥氏体不锈钢产品及其制造方法
EP3878983A1 (en) * 2012-01-20 2021-09-15 Solu Stainless Oy Method for manufacturing an austenitic stainless steel product
CN103484779A (zh) * 2013-09-05 2014-01-01 常熟市勤丰铸件厂 一种不锈钢铸件
CN106011681A (zh) * 2016-06-27 2016-10-12 武汉科技大学 一种提高316ln奥氏体不锈钢力学性能的方法
CN111727269A (zh) * 2018-03-15 2020-09-29 日铁不锈钢株式会社 马氏体系不锈钢板及其制造方法以及弹簧构件
CN113637924A (zh) * 2020-04-27 2021-11-12 靖江市中信特种机械泵阀厂 一种醪液泵新型材料
CN114480977A (zh) * 2021-12-13 2022-05-13 四川大学 一种低温2500MPa级超高强高韧钢及其制备方法
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CN115595420B (zh) * 2022-12-13 2023-03-21 太原科技大学 一种高强韧含铜不锈钢及其生产工艺
CN118241037A (zh) * 2024-05-29 2024-06-25 太原科技大学 一种具有双峰组织的含铜不锈钢及其制备方法

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HUE042000T2 (hu) 2019-06-28
EP2245203B1 (fr) 2018-10-31
DK2245203T3 (en) 2019-02-18
PT2245203T (pt) 2019-02-06
ES2708578T3 (es) 2019-04-10
EP2245203A1 (fr) 2010-11-03
TR201900950T4 (tr) 2019-02-21
WO2009101285A1 (fr) 2009-08-20
PL2245203T3 (pl) 2019-06-28

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