EP1339880B1 - Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid - Google Patents

Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid Download PDF

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Publication number
EP1339880B1
EP1339880B1 EP01996631A EP01996631A EP1339880B1 EP 1339880 B1 EP1339880 B1 EP 1339880B1 EP 01996631 A EP01996631 A EP 01996631A EP 01996631 A EP01996631 A EP 01996631A EP 1339880 B1 EP1339880 B1 EP 1339880B1
Authority
EP
European Patent Office
Prior art keywords
strip
heat treatment
steel
process according
hardening heat
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.)
Expired - Lifetime
Application number
EP01996631A
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German (de)
English (en)
French (fr)
Other versions
EP1339880A1 (fr
Inventor
Lucien Coutu
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 Alloys Imphy SAS
Original Assignee
Imphy Alloys 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 Imphy Alloys SA filed Critical Imphy Alloys SA
Publication of EP1339880A1 publication Critical patent/EP1339880A1/fr
Application granted granted Critical
Publication of EP1339880B1 publication Critical patent/EP1339880B1/fr
Priority to CY20071101302T priority Critical patent/CY1106925T1/el
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • 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
    • C21D8/0221—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 characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D8/0247—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 characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing

Definitions

  • the present invention relates to a maraging steel particularly suitable for the manufacture of parts requiring a very good resistance to fatigue.
  • maraging steels having different chemical compositions and mechanical characteristics, such as maraging steels containing 18% of nickel, 12% of cobalt, 4% of molybdenum, 1.6% titanium and 0.2% aluminum, or maraging steels containing 18% nickel, 3% molybdenum, 1.4% titanium and 0.1% aluminum, or maraging steels containing 13% chromium, 8% nickel, 2% molybdenum and 1% aluminum. But none of these steels gave satisfactory results. Fatigue suits are always lower than those made with the usual steel.
  • the object of the present invention is to overcome this disadvantage and to propose a band or piece of maraging steel having improved fatigue strength.
  • the subject of the invention is a method for manufacturing a strip or a piece cut from a cold-rolled maraging steel strip. According to this process, before carrying out the curing heat treatment, the strip or the part is subjected to a cold plastic deformation with a hardening rate greater than 30% and the strip or part is annealed. of recrystallization so as to obtain a fine grain of ASTM index greater than 8.
  • the chemical composition of the steel comprises, by weight: 12 % ⁇ Or ⁇ 24 , 5 % 2 , 5 % ⁇ MB ⁇ 12 % 4 , 17 % ⁇ Co ⁇ 20 % al % ⁇ 0 , 15 % Ti ⁇ 0 , 1 % NOT ⁇ 0 , 003 % Yes ⁇ 0 , 1 % mn ⁇ 0 , 1 % VS ⁇ 0 , 005 % S ⁇ 0 , 001 % P ⁇ 0 , 005 % H ⁇ 0 , 0003 % O ⁇ 0 , 001 % the rest being iron and impurities resulting from the preparation, the chemical composition further satisfying the relations: 20 % ⁇ Or + MB ⁇ 27 % 50 ⁇ Co ⁇ MB ⁇ 200 Ti ⁇ NOT ⁇ 2 ⁇ 10 - 4
  • the strip or the part is subjected to cold rolling with a reduction rate of between 1% and 10%.
  • the maraging steel is remelted under vacuum by the VAR method or remelted a first time under vacuum by the VAR method or electroconductive slag by the ESR process and remelted a second time under vacuum by the VAR method.
  • the invention also relates to a strip or piece, less than 1 mm thick, maraging steel having a fine grain ASTM index greater than 8 and a yield strength after curing greater than 1850 MPa.
  • the strip or the piece thus obtained can be used for the manufacture of parts such as belts. These pieces are cured by a curing treatment at 450-550 ° C for 1-10 hours which may be followed by surface nitriding.
  • the steel is made by targeting a carbon less than 0.005% and then deoxidizing aluminum.
  • the steel thus produced is cast in the form of reflow electrodes.
  • These electrodes are either remelted under vacuum (VAR method, “Vacuum Arc Remelting” known in itself) to form ingots or slabs, or remelted under vacuum (VAR) or electrically conductive slag (ESR process, "Electro Slag Remelting ", known in itself) to form second electrodes which are themselves remelted under vacuum (VAR) to form ingots or slabs.
  • VAR method "Vacuum Arc Remelting” known in itself
  • VAR remelted under vacuum
  • ESR process Electrically conductive slag Remelting
  • the ingots or slabs are then hot-rolled after reheating at about 1200 ° C., and for example between 1150 ° C. and 1250 ° C. to obtain hot-rolled strips a few millimeters thick, and for example about 4 , 5 mm thick.
  • the hot rolled strips are pickled then cold rolled with one or more recrystallization anneals to obtain cold-rolled strips less than 1 mm thick, for example 0.4 mm or 0.2 mm thick. .
  • the last intermediate recrystallization annealing treatment is carried out at such a thickness that the cold rolled strip has a work hardening rate of greater than 30% and more preferably greater than 40%.
  • the thus-hardened strip is annealed, for example in the passage oven, to obtain a fine grain of ASTM index greater than 8 (corresponding to an average grain diameter of less than 20 microns), and better than 10 (corresponding to a diameter average grain less than 10 microns); the grain size being determined according to ASTM E112.
  • the annealing treatment intended to obtain a fine grain is carried out under a protective atmosphere by suitably adjusting the temperature and duration parameters. These parameters depend on the particular conditions of realization of the heat treatment and those skilled in the art know how to determine these parameters in each particular case.
  • the duration ie the residence time of any point of the strip in the oven
  • the set temperature of the oven is between 900 ° C and 1100 ° C
  • the furnace atmosphere may be argon with a lower dew temperature preferably at -50 ° C.
  • the band can, in addition, be subjected to a light cold rolling with a reduction ratio of between 1% and 10%, which leads to a work hardening rate of the same value.
  • the hardening treatment may also be carried out in the oven at a temperature of between 600 ° C. and 700 ° C. for a time of between 30 seconds and 3 minutes.
  • the part can be cured on the surface by a nitriding treatment carried out by maintaining a few hours at 500 ° C in a nitrogen-rich reactive gas mixture.
  • blanks of parts may be cut into cold-rolled strips of greater thickness than the desired final thickness for the parts. These blanks are shaped, possibly welded, then cold rolled to the final thickness so as to have a work hardening rate greater than 30% or better than 40%. The parts are then annealed under the same conditions as described above, so as to obtain a fine grain of ASTM index greater than 8, or better than 10, and then subjected to a hardening treatment as indicated below. above. The yield strength obtained is high and the resistance to fatigue is excellent.
  • Pieces can also be made by cutting, for example by chemical cutting, into hardened strips. The entire process, including the curing heat treatment, is then applied to the web. These parts are, for example, integrated circuit support grids.
  • the contents of nickel and molybdenum must be such that 20% ⁇ Ni + Mo ⁇ 27%, and preferably such that 22% ⁇ Ni + Mo ⁇ 25%.
  • the cobalt and molybdenum contents In order to obtain a yield strength, after curing heat treatment, greater than 1850 MPa, the cobalt and molybdenum contents must be such that Co x Mo ⁇ 50, and preferably such that Co x Mo ⁇ 70. Indeed the higher the product, the higher the yield strength. But, in order to obtain sufficient ductility, the cobalt and molybdenum contents must be such that Co x Mo ⁇ 200, and preferably such that Co x Mo ⁇ 120. These values respectively correspond to yield strengths of less than approximately 3000 MPa. and 2500 MPa.
  • the residual elements must be rigorously controlled to obtain good ductility and fatigue resistance properties. These limitations include: al % ⁇ 0 , 15 % Ti ⁇ 0 , 1 % NOT ⁇ 0 , 003 % Yes ⁇ 0 , 1 % mn ⁇ 0 , 1 % VS ⁇ 0 , 005 % S ⁇ 0 , 001 % P ⁇ 0 , 005 % H ⁇ 0 , 0003 % O ⁇ 0 , 001 %
  • the minimum content may be 0% or traces.
  • the nitrogen and titanium contents must be such that: Ti x N ⁇ 2 x 10 -4 , or better, ⁇ 1 x 10 -4 .
  • a first band A given by way of example, was annealed with hydrogen passage at 1020 ° C for 1 minute to obtain a fine grain of ASTM 11 index and then cured by holding at 490 ° C for 3 hours.
  • a second strip B given for comparison, was pass-annealed at 1150 ° C for 1 minute to obtain a coarse grain of ASTM 7 index and then cured by holding at 490 ° C for 3 hours.
  • the fatigue limit was greater than 8 ⁇ 10 8 cycles, whereas for the band B the fatigue limit was 5 ⁇ 10 8 cycles.
  • Both bands A and B had a yield strength greater than 1850 MPa.
  • a maraging steel strip containing 18% nickel, 9% cobalt and 5% molybdenum was also manufactured. 0.5% titanium and 0.1% aluminum.
  • This tape was made by the process according to the invention, the grain had an ASTM index of 10 and the yield strength was 1910 MPa. The fatigue limit measured under the same test conditions as in the previous case was 2 x 10 8 cycles.
  • These strips can advantageously be used to manufacture belts or any other product, such as integrated circuit support grids.
  • transmission belts for an internal combustion engine consisting of jumpers held by rings consisting of narrow strips in accordance with the invention and whose two ends are welded have been manufactured.
  • These belts have a lifespan more than ten times longer than the life of identical belts but manufactured with maraging steel strips according to the prior art.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Articles (AREA)
EP01996631A 2000-11-17 2001-11-16 Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid Expired - Lifetime EP1339880B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CY20071101302T CY1106925T1 (el) 2000-11-17 2007-09-10 Διαδικασια για την κατασκευη μιας ταινιας ή ενος τεμαχιου που κοβεται απο μια ταινια χαλυβα μαρτεγηρανσης ψυχρης ελασης

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0014807A FR2816959B1 (fr) 2000-11-17 2000-11-17 Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid
FR0014807 2000-11-17
PCT/FR2001/003595 WO2002040722A1 (fr) 2000-11-17 2001-11-16 Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid

Publications (2)

Publication Number Publication Date
EP1339880A1 EP1339880A1 (fr) 2003-09-03
EP1339880B1 true EP1339880B1 (fr) 2007-07-11

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EP01996631A Expired - Lifetime EP1339880B1 (fr) 2000-11-17 2001-11-16 Procede pour fabriquer une bande ou une piece decoupee dans une bande en acier maraging laminee a froid

Country Status (16)

Country Link
US (1) US6663730B2 (https=)
EP (1) EP1339880B1 (https=)
JP (2) JP4278378B2 (https=)
KR (2) KR20080048544A (https=)
CN (1) CN1298869C (https=)
AR (1) AR034276A1 (https=)
AT (1) ATE366826T1 (https=)
AU (1) AU2002218382A1 (https=)
CY (1) CY1106925T1 (https=)
DE (1) DE60129350T2 (https=)
DK (1) DK1339880T3 (https=)
ES (1) ES2287187T3 (https=)
FR (1) FR2816959B1 (https=)
PT (1) PT1339880E (https=)
TW (1) TW539746B (https=)
WO (1) WO2002040722A1 (https=)

Cited By (2)

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Publication number Priority date Publication date Assignee Title
WO2016170397A1 (fr) 2015-04-23 2016-10-27 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication
WO2017064537A1 (fr) 2015-10-15 2017-04-20 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication

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CN107419196B (zh) * 2017-09-18 2019-12-20 东北大学 屈强比可控的超低碳易焊接中锰汽车用钢及其制备方法
JP2019189927A (ja) * 2018-04-27 2019-10-31 トヨタ自動車株式会社 無端金属リング、及びその製造方法
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CN117597460A (zh) * 2021-07-01 2024-02-23 山特维克加工解决方案股份有限公司 用于增材制造的粉末、其用途和增材制造方法
CN113774289A (zh) * 2021-08-25 2021-12-10 哈尔滨工程大学 一种2700MPa级高塑韧性高耐蚀马氏体时效不锈钢及其制备方法
CN115786813B (zh) * 2022-11-09 2024-06-11 成都先进金属材料产业技术研究院股份有限公司 一种马氏体时效钢板材及其制备方法

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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016170397A1 (fr) 2015-04-23 2016-10-27 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication
WO2016170519A1 (fr) 2015-04-23 2016-10-27 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication
WO2017064537A1 (fr) 2015-10-15 2017-04-20 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication
WO2017064684A1 (fr) 2015-10-15 2017-04-20 Aperam Acier, produit réalisé en cet acier, et son procédé de fabrication
CN108138286A (zh) * 2015-10-15 2018-06-08 艾普伦 钢、所述钢制造的产品及其制造方法
US10731231B2 (en) 2015-10-15 2020-08-04 Aperam Steel, product created from said steel, and manufacturing method thereof
CN116024505A (zh) * 2015-10-15 2023-04-28 艾普伦 钢、所述钢制造的产品及其制造方法
CN116024505B (zh) * 2015-10-15 2025-04-11 艾普伦 钢、所述钢制造的产品及其制造方法

Also Published As

Publication number Publication date
CY1106925T1 (el) 2012-09-26
JP2008274436A (ja) 2008-11-13
EP1339880A1 (fr) 2003-09-03
ATE366826T1 (de) 2007-08-15
KR20030055303A (ko) 2003-07-02
FR2816959A1 (fr) 2002-05-24
AR034276A1 (es) 2004-02-18
JP4278378B2 (ja) 2009-06-10
US20020059967A1 (en) 2002-05-23
AU2002218382A1 (en) 2002-05-27
ES2287187T3 (es) 2007-12-16
PT1339880E (pt) 2007-08-13
TW539746B (en) 2003-07-01
US6663730B2 (en) 2003-12-16
DK1339880T3 (da) 2007-09-10
KR100884639B1 (ko) 2009-02-23
DE60129350D1 (de) 2007-08-23
JP4965502B2 (ja) 2012-07-04
CN1298869C (zh) 2007-02-07
DE60129350T2 (de) 2008-03-13
FR2816959B1 (fr) 2003-08-01
JP2004514056A (ja) 2004-05-13
WO2002040722A1 (fr) 2002-05-23
KR20080048544A (ko) 2008-06-02
CN1630732A (zh) 2005-06-22

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