EP0474530B1 - Verfahren zum Herstellen von hoch bruchfesten Produkten aus instabilem austenitischem Stahl und so hergestellte Produkte - Google Patents

Verfahren zum Herstellen von hoch bruchfesten Produkten aus instabilem austenitischem Stahl und so hergestellte Produkte Download PDF

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Publication number
EP0474530B1
EP0474530B1 EP91402232A EP91402232A EP0474530B1 EP 0474530 B1 EP0474530 B1 EP 0474530B1 EP 91402232 A EP91402232 A EP 91402232A EP 91402232 A EP91402232 A EP 91402232A EP 0474530 B1 EP0474530 B1 EP 0474530B1
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European Patent Office
Prior art keywords
steel
deformation
tensile strength
temperature
martensite
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Expired - Lifetime
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EP91402232A
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English (en)
French (fr)
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EP0474530A1 (de
Inventor
Jean-Michel Hauser
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.)
Ugitech SA
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Ugine Savoie SA
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    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys

Definitions

  • the present invention relates to a process for producing products with a very high breaking load from an unstable austenitic steel, and the product obtained by this process, in particular in the form of a wire or strip.
  • This process is of the type in which the steel is subjected to a first plastic deformation at a temperature higher than the limit temperature (Md) of formation of martensite by deformation and lower than the recrystallization temperature and then to a second deformation of said steel to a temperature lower than said temperature (Md).
  • hot-rolled steel prior to the first deformation, is subjected to a standard annealing heat treatment known as hyper-hardening consisting in placing said steel at a temperature between 1000 and 1100 ° C for about 30 minutes.
  • hyper-hardening consisting in placing said steel at a temperature between 1000 and 1100 ° C for about 30 minutes.
  • the object of the invention is to control the formation of martensite so as to obtain products with particularly high tensile characteristics.
  • the steel in a first step, is subjected to plastic deformation at a temperature above the limit temperature (Md) for the formation of martensite by deformation and below the recrystallization temperature.
  • Md limit temperature
  • the breaking load of the steel is greater than 1000 MPa, preferably greater than 1300 MPa.
  • the steel is deformed at a temperature below (Md), in a determined range of martensite formation temperature so that for an additional rational deformation of 0.1, the increase in the rate of martensite formed does not exceed 20% at any time.
  • the steel is deformed at a temperature below (Md) with a cumulative rational deformation of between 0.7 and 3, which corresponds to a reduction rate of section included between 50 and 95%.
  • a minimum cumulative rational deformation of 0.7 is necessary to reach or slightly exceed the breaking loads envisaged in the drawing processes of the prior art.
  • the steel is subjected to an aging treatment.
  • the reduction rate can be much higher than this minimum rate.
  • the products with very high breaking load according to the invention in particular in the form of wire or strip, are obtained by a plasticity effect induced by deformation.
  • Aging of steels subjected to warm work hardening, followed by cold work hardening according to the process can increase the breaking load by around 200 MPa and sometimes more depending on the grade of steel used.
  • the conditions for obtaining high tensile strengths are attached on the one hand to the mechanical characteristics obtained during lukewarm hardening, the steel having to have at least one tensile strength greater than 1000 MPa and on the other hand to the conditions of cold work hardening, according to which the work hardening of the steel is carried out in a determined temperature range, called critical field of temperature of deformation of martensite, so that for an additional rational formation of 0.1, the increase in the rate of martensite formed does not exceed, at any time, 20%.
  • rational deformation is meant the logarithm of the ratio of the surface S of the section after deformation on the surface So of the initial section (ln S / So).
  • the determined range of martensite formation temperature is, for the steels taken as an example, included in the range -20 ° C. + 180 ° C. Indeed, beyond + 180 ° C there is no longer an appreciable amount of martensite, while below -20 ° C the formation of martensite is excessive.
  • the basic thread used in these three examples is a wire rod about 5.6mm in diameter; the wire is cold-worked at 250 ° C in several passes up to a diameter of approximately 2mm, then this wire is cold drawn at room temperature of 20 ° C in order to obtain a wire of approximately 0.5mm in diameter, the section reduction rates per drawing pass being approximately 25%. After each drawing pass the wire returns to room temperature before another pass.
  • the number of lukewarm passes is approximately 20, the number of cold passes being approximately 10.
  • the steel used for the implementation of the process is a steel referenced 1, having the following composition by weight: 0.08% of carbon, 18.6% of chromium, 8.5% of nickel, 0.3% of manganese , 0.5% silicon, 0.04% nitrogen.
  • Curve 1A represents, for the steel referenced 1, the evolution of the rate of martensite as a function of the rational deformation, this rate of martensite reaching around 60% after cold drawing.
  • Curve 1B represents the evolution of the load at break during lukewarm hardening up to 1400 MPa then the evolution of the load at break during cold drawing thus reaching 2500 MPa; aging provides a breaking load of approximately 2700 Mpa.
  • the increase in the breaking load is obtained by controlling the increase in the formation of martensite from one wire drawing pass to another.
  • the steel used is a steel referenced 2, having the following weight composition: 0.09% carbon, 17.3% chromium, 8.3% nickel, 0.9% manganese, 0.8% silicon , 0.06% nitrogen.
  • Curve 2A illustrates for the steel referenced 2 the evolution of the rate of martensite as a function of the cumulative rational deformation, the rate of martensite reached being around 45%.
  • Curve 2B represents the evolution of the breaking load during lukewarm hardening, up to a breaking load of 1600 MPa, then the evolution of said breaking load during cold drawing, reaching about 2500 MPa.
  • the steel used is a steel referenced 3 and having the following composition: 0.09% carbon, 17.3% chromium, 7.7% nickel, 0.5% manganese, 0.8% silicon, 0.15% nitrogen, 1% aluminum.
  • the curve 3A represents for the steel referenced 3 the evolution of the rate of martensite as a function of the rational deformation, the rate of martensite being able to reach 95%.
  • Curve 3B represents the evolution of the breaking load during lukewarm hardening, up to the breaking load of approximately 1600 MPa, then the evolution of said breaking load during cold drawing, reaching around 2300 Mpa.
  • the gain after heat treatment at 480 ° C for 45 minutes is in this example about 300 MPa.
  • Such characteristics are obtained by the formation of martensite during cold drawing, slower formation on a product previously cold-worked at lukewarm than by direct cold drawing of the wire rod.
  • the first “lukewarm” deformation or work hardening operation may be a wire drawing, as described in the examples, but also a rolling, hammering or forging, twisting, alternating bending, or the like.
  • the second cold deformation operation can also take various aspects: drawing, rolling or other.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)

Claims (9)

  1. Verfahren zur Herstellung von Produkten mit sehr hoher Bruchfestigkeit ausgehendvon einem instabilen austenitischen Stahl, gemäß dem der Stahl einer ersten plastischen Deformation bei einer Temperatur oberhalb der Grenztemperatur (Md) der Bildung von Martensit durch Deformation und unterhalb der Rekristallisationstemperatur unterworfen wird und dieser Stahl dann einer zweiten Deformation bei einer Temperatur unterhalb dieser Grenztemperatur (Md) unterworfen wird, dadurch gekennzeichnet, daß der Stahl bei der zweiten Deformation in einem bestimmten Bereich der Bildungstemperatur von Martensit derart verformt wird, daß bei einer zusätzlichen rationellen Deformation von 0,1 die Zunahme des Anteils an gebildetem Martensit in jedem Augenblick 20% nicht übersteigt.
  2. Verfahren nach Anspruch 1, dadurch gekennzeichnet, daß der Stahl bei einer Temperatur unterhalb (Md) bei einer kumulierten rationellen Deformation zwischen 0,7 und 3 verformt wird.
  3. Verfahren nach Anspruch 1, dadurch gekennzeichnet, daß der Stahl nach der zweiten Deformation einer Alterungsbehandlung unterworfen wird.
  4. Verfahren nach Anspruch 1, dadurch gekennzeichnet, daß die erste plastische Deformation mit einer rationellen Deformation von mehr als 1,65 sichergestellt wird.
  5. Verfahren nach den Ansprüchen 1 und 4, dadurch gekennzeichnet, daß die Bruchfestigkeit des Stahls nach der ersten plastischen Deformation oberhalb 1300 MPa liegt.
  6. Produkt mit sehr hoher Bruchfestigkeit, erhalten ausgehend von einem instabilen austenitischen Stahl insbesondere in Form eines Drahtes oder Bandes, dadurch gekennzeichnet, daß es nach dem Verfahren gemäß einem der Ansprüche 1 bis 5 hergestellt worden ist, der austenitische Stahl ein Stahl der folgenden Zusammensetzung ist:
       0,01 bis 0,15 % Kohlenstoff,
       13 bis 23 % Chrom,
       5 bis 13 % Nickel,
       0,2 bis 2,5 % Mangan,
       0,2 bis 3 % Silicium,
       0,01 bis 0,15 % Stickstoff
       gegebenenfalls 0,5 bis 2 % Aluminium und weniger als 2 % Molybdän,
       und Eisen als Rest, und
    daß seine Bruchfestigkeit vor dem Altern größer als 2300 MPa ist.
  7. Produkt mit sehr hoher Bruchfestigkeit, erhalten ausgehend von einem instabilen austenitischen Stahl insbesondere in Form eines Drahtes oder Bandes, dadurch gekennzeichnet, daß es nach dem Verfahren gemäß einem der Ansprüche 1 bis 5 hergestellt worden ist, der austenitische Stahl ein Stahl der folgenden Zusammensetzung ist:
       0,2 bis 1 % Kohlenstoff,
       15 bis 30 % Mangan,
       0,01 bis 0,7 % Stickstoff,
       gegebenenfalls weniger als 5 % Chrom und weniger als 7 % Aluminium,
       und Eisen als Rest, und
    daß seine Bruchfestigkeit vor dem Altern mehr als 2300 MPa beträgt.
  8. Produkt mit sehr hoher Bruchfestigkeit, erhalten ausgehend von einem instabilen austenitischen Stahl insbesondere in Form eines Drahtes oder Bandes, dadurch gekennzeichnet, daß es nach dem Verfahren gemäß einem der Ansprüche 1 bis 5 hergestellt worden ist, der austenitische Stahl ein Stahl der folgenden Zusammensetzung ist:
       0,1 bis 0,6 % Kohlenstoff,
       6 bis 25 % Nickel,
       0 bis 13 % Chrom,
       0 bis 4 % Molybdän,
       0 bis 3 % Silicium
       und Eisen als Rest, und
    daß seine Bruchfestigkeit vor dem Altern mehr als 2300 MPa beträgt.
  9. Produkt nach einem der Ansprüche 6 bis 8, dadurch gekennzeichnet, daß seine Bruchfestigkeit nach dem Altern mehr als 2500 MPa beträgt.
EP91402232A 1990-08-30 1991-08-12 Verfahren zum Herstellen von hoch bruchfesten Produkten aus instabilem austenitischem Stahl und so hergestellte Produkte Expired - Lifetime EP0474530B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9010828 1990-08-30
FR9010828A FR2666352B1 (fr) 1990-08-30 1990-08-30 Procede d'elaboration de produits a tres haute charge a la rupture a partir d'un acier austhenitique instable, et produits en resultant.

Publications (2)

Publication Number Publication Date
EP0474530A1 EP0474530A1 (de) 1992-03-11
EP0474530B1 true EP0474530B1 (de) 1995-12-13

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EP91402232A Expired - Lifetime EP0474530B1 (de) 1990-08-30 1991-08-12 Verfahren zum Herstellen von hoch bruchfesten Produkten aus instabilem austenitischem Stahl und so hergestellte Produkte

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EP (1) EP0474530B1 (de)
JP (1) JPH0681033A (de)
AT (1) ATE131539T1 (de)
CA (1) CA2050208C (de)
DE (1) DE69115392T2 (de)
ES (1) ES2083543T3 (de)
FR (1) FR2666352B1 (de)
GR (1) GR3019185T3 (de)
PT (1) PT98792B (de)
TW (1) TW226033B (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102004051885A1 (de) * 2004-10-26 2006-04-27 Fag Kugelfischer Ag & Co. Ohg Mechanisch belastbares Stell- oder Lagerbauteil aus mechanisch gehärtetem Stahl

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62275035A (ja) * 1985-05-07 1987-11-30 Sumitomo Electric Ind Ltd 光フアイバ用母材の製造方法
JP3542239B2 (ja) * 1996-10-15 2004-07-14 新日本製鐵株式会社 耐伸線縦割れ性に優れた高強度ステンレス線材及びその鋼線
FR2778188B1 (fr) * 1998-04-29 2000-06-02 Ugine Savoie Sa Acier inoxydable pour l'elaboration de fil trefile notamment de fil de renfort de pneumatique et procede de realisation dudit fil
JP4519513B2 (ja) * 2004-03-08 2010-08-04 新日鐵住金ステンレス株式会社 剛性率に優れた高強度ステンレス鋼線およびその製造方法
WO2010052751A1 (en) * 2008-11-05 2010-05-14 Honda Motor Co., Ltd. High-strength steel sheet and the method for production therefor
EP4198363A1 (de) * 2021-12-14 2023-06-21 Vallourec Tube-Alloy, LLC Hochfestes isoliertes rohr

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3296846A (en) * 1964-06-05 1967-01-10 Crucible Steel Co America Method of rolling steel
US3488231A (en) * 1966-11-22 1970-01-06 Atomic Energy Commission Treatment of steel
US3871925A (en) * 1972-11-29 1975-03-18 Brunswick Corp Method of conditioning 18{14 8 stainless steel
US4265679A (en) * 1979-08-23 1981-05-05 Kawasaki Steel Corporation Process for producing stainless steels for spring having a high strength and an excellent fatigue resistance
US4415377A (en) * 1982-06-28 1983-11-15 Olin Corporation Duplex rolling process and apparatus

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102004051885A1 (de) * 2004-10-26 2006-04-27 Fag Kugelfischer Ag & Co. Ohg Mechanisch belastbares Stell- oder Lagerbauteil aus mechanisch gehärtetem Stahl

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DE69115392T2 (de) 1996-05-30
GR3019185T3 (en) 1996-06-30
TW226033B (de) 1994-07-01
PT98792A (pt) 1992-07-31
FR2666352B1 (fr) 1992-12-11
FR2666352A1 (fr) 1992-03-06
JPH0681033A (ja) 1994-03-22
CA2050208A1 (fr) 1992-03-01
ATE131539T1 (de) 1995-12-15
EP0474530A1 (de) 1992-03-11
ES2083543T3 (es) 1996-04-16
CA2050208C (fr) 2002-08-20
PT98792B (pt) 1999-01-29
DE69115392D1 (de) 1996-01-25

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