EP1339880B1 - Method for making a strip or a workpiece cut out from a cold rolled maraging steel strip - Google Patents
Method for making a strip or a workpiece cut out from a cold rolled maraging steel strip Download PDFInfo
- 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
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- 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
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- 238000000034 method Methods 0.000 title claims description 22
- 229910001240 Maraging steel Inorganic materials 0.000 title claims description 16
- 229910000831 Steel Inorganic materials 0.000 claims description 14
- 239000010959 steel Substances 0.000 claims description 14
- 239000000203 mixture Substances 0.000 claims description 12
- 238000010438 heat treatment Methods 0.000 claims description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 10
- 229910052719 titanium Inorganic materials 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- 238000005121 nitriding Methods 0.000 claims description 9
- 239000000126 substance Substances 0.000 claims description 8
- 229910052739 hydrogen Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 238000001953 recrystallisation Methods 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 6
- 238000000137 annealing Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 229910052760 oxygen Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 238000005097 cold rolling Methods 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 230000005540 biological transmission Effects 0.000 claims description 2
- 238000003723 Smelting Methods 0.000 claims 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 29
- 229910052750 molybdenum Inorganic materials 0.000 description 14
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 13
- 239000011733 molybdenum Substances 0.000 description 12
- 239000010936 titanium Substances 0.000 description 10
- 229910017052 cobalt Inorganic materials 0.000 description 9
- 239000010941 cobalt Substances 0.000 description 9
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 9
- 229910052759 nickel Inorganic materials 0.000 description 8
- 230000002349 favourable effect Effects 0.000 description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000002893 slag Substances 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000008685 targeting Effects 0.000 description 1
- 238000010313 vacuum arc remelting Methods 0.000 description 1
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 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
- 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
-
- 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 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
- C21D8/0221—Modifying the physical properties 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 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
- C21D8/0247—Modifying the physical properties 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)
- Heat Treatment Of Articles (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
- Soft Magnetic Materials (AREA)
Description
La présente invention est relative à un acier maraging particulièrement adapté à la fabrication de pièces nécessitant une très bonne résistance à la fatigue.The present invention relates to a maraging steel particularly suitable for the manufacture of parts requiring a very good resistance to fatigue.
De nombreuses pièces sont fabriquées à partir de bandes en acier maraging contenant, en % en poids, environ 18% de nickel, 9% de cobalt, 5% de molybdène, 0,5% de titane et 0,1% d'aluminium, traité pour avoir une limite d'élasticité supérieure à 1800 MPa. Ces bandes sont obtenues par laminage à chaud et laminage à froid. Les bandes ou les pièces découpées dans les bandes sont ensuite durcies par un traitement thermique de durcissement vers 500°C. Les pièces sont éventuellement nitrurées en surface pour améliorer leur tenue en fatigue. Cependant la tenue en fatigue de ces pièces est insuffisante.Many parts are made from maraging steel strips containing, in% by weight, about 18% nickel, 9% cobalt, 5% molybdenum, 0.5% titanium and 0.1% aluminum, treated to have a yield strength greater than 1800 MPa. These strips are obtained by hot rolling and cold rolling. The strips or cut pieces in the strips are then cured by a curing heat treatment at about 500 ° C. The pieces are optionally nitrided on the surface to improve their fatigue resistance. However the fatigue resistance of these parts is insufficient.
Afin d'améliorer la tenue en fatigue des pièces, il a été envisagé d'utiliser des aciers maraging ayant des compositions chimiques et des caractéristiques mécaniques différentes, telles que des aciers maraging contenant 18% de nickel, 12 % de cobalt, 4% de molybdène, 1,6% de titane et 0,2% d'aluminium, ou des aciers maraging contenant 18 % de nickel, 3% de molybdène, 1,4% de titane et 0,1% d'aluminium, ou encore, des aciers maraging contenant 13% de chrome, 8% de nickel, 2% de molybdène et 1 % d'aluminium. Mais aucun de ces aciers n'a donné de résultats satisfaisants. Les tenues à la fatigue étant toujours inférieures à celle des pièces fabriquées avec l'acier habituel.In order to improve the fatigue strength of the parts, it has been envisaged to use 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.
Le but de la présente invention est de remédier à cet inconvénient et de proposer une bande ou une pièce en acier maraging ayant une tenue à la fatigue améliorée.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.
A cet effet, l'invention a pour objet un procédé pour de fabrication d'une bande ou une pièce découpée dans une bande en acier maraging laminée à froid. Selon ce procédé, avant d'effectuer le traitement thermique de durcissement, on soumet la bande ou la pièce à une déformation plastique à froid avec un taux d'écrouissage supérieur à 30% et on et on soumet la bande ou la pièce à un recuit de recristallisation de façon à obtenir un grain fin d'indice ASTM supérieur à 8. La composition chimique de l'acier comprend, en poids :
Eventuellement, après le recuit de recristallisation, on soumet la bande ou la pièce à un laminage à froid avec un taux de réduction compris ente 1% et 10%.Optionally, after the recrystallization annealing, the strip or the part is subjected to cold rolling with a reduction rate of between 1% and 10%.
De préférence, l'acier maraging est refondu sous vide par le procédé VAR ou refondu une première fois sous vide par le procédé VAR ou sous laitier électroconducteur par le procédé ESR et refondu une seconde fois sous vide par le procédé VAR.Preferably, 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.
L'invention concerne également une bande ou pièce, d'épaisseur inférieure à 1 mm, en acier maraging ayant un grain fin d'indice ASTM supérieur à 8 et une limite d'élasticité après durcissement supérieure à 1850 MPa.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.
La bande ou la pièce ainsi obtenue peut être utilisée pour la fabrication de pièces telles que des courroies. Ces pièces sont durcies par un traitement de durcissement entre 450 et 550°C pendant 1 à 10 heures qui peut être suivi d'une nitruration en surface.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.
L'invention va maintenant être décrite plus en détails mais de façon non limitative.The invention will now be described in more detail but in a nonlimiting manner.
Pour fabriquer une bande laminée à froid en acier maraging selon l'invention, on élabore l'acier en visant un carbone inférieur à 0,005% puis en désoxydant à l'aluminium.To manufacture a cold rolled strip of maraging steel according to the invention, the steel is made by targeting a carbon less than 0.005% and then deoxidizing aluminum.
L'acier ainsi élaboré est coulé sous forme d'électrodes de refusion. Ces électrodes sont soit refondues sous vide (procédé VAR, « Vacuum Arc Remelting » connu en lui-même) pour former des lingots ou des brames, soit refondues une première fois sous vide (VAR) ou sous laitier électroconducteur (procédé ESR, « Electro Slag Remelting », connu en lui-même) pour former des secondes électrodes qui sont elles-mêmes refondues sous vide (VAR) pour former des lingots ou des brames. On réalise ainsi soit une simple refusion VAR soit une double refusion VAR + VAR ou ESR + VAR. Ces refusions permettent d'épurer le métal et d'améliorer la qualité de la solidification en réduisant les ségrégations. En particulier, la refusion ESR permet d'abaisser la teneur en soufre, et la refusion VAR permet d'abaisser la teneur en azote et en hydrogène.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. This is done either a simple VAR reflow or a double reflow VAR + VAR or ESR + VAR. These refusals make it possible to purify the metal and to improve the quality of the solidification by reducing the segregations. In particular, ESR remelting makes it possible to lower the sulfur content, and VAR remelting makes it possible to lower the nitrogen and hydrogen content.
Les lingots ou brames sont alors laminés à chaud après réchauffage aux environs de 1200°C, et par exemple entre 1150°C et 1250°C pour obtenir des bandes laminées à chaud de quelques millimètres d'épaisseur, et par exemple d'environ 4,5 mm d'épaisseur.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.
Les bandes laminées à chaud sont décapées puis laminées à froid avec un ou plusieurs recuits de recristallisation pour obtenir des bandes laminées à froid d'épaisseur inférieure à 1 mm, et par exemple de 0,4 mm ou de 0,2 mm d'épaisseur.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. .
Le dernier traitement de recuit de recristallisation intermédiaire est effectué à une épaisseur telle que la bande laminée à froid ait un taux d'écrouissage supérieur à 30% et mieux supérieur à 40%.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%.
La bande ainsi écrouie est recuite, par exemple au four à passage, pour obtenir un grain fin d'indice ASTM supérieur à 8 (correspondant à un diamètre moyen des grains inférieur à 20 microns), et mieux supérieur à 10 (correspondant à un diamètre moyen des grains inférieur à 10 microns); la taille de grain étant déterminée selon la norme ASTM E112.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.
Le traitement de recuit destiné à obtenir un grain fin est réalisé sous atmosphère protectrice en ajustant convenablement les paramètres température et durée. Ces paramètres dépendent des conditions particulières de réalisation du traitement thermique et l'homme du métier sait déterminer ces paramètres dans chaque cas particulier. Dans le cas d'un traitement réalisé dans un four à passage en continu, la durée (c'est à dire le temps de séjour d'un point quelconque de la bande dans le four) est comprise entre 10s et 1 minute, et la température de consigne du four est comprise entre 900°C et 1100°C; l'atmosphère du four peut être de l'argon avec une température de rosée inférieure de préférence à - 50°C.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. In the case of a treatment carried out in a continuous passage furnace, the duration (ie the residence time of any point of the strip in the oven) is between 10s and 1 minute, and 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.
Afin d'améliorer la planéité de la bande et, si nécessaire, de parfaire la transformation martensitique, la bande peut, en outre, être soumise à un laminage à froid léger avec un taux de réduction compris entre 1 % et 10%, ce qui conduit à un taux d'écrouissage de même valeur.In order to improve the flatness of the band and, if necessary, to perfect the martensitic transformation, 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.
On peut alors découper dans la bande une pièce et mettre en forme cette pièce, par exemple par pliage, puis effectuer sur celle-ci un traitement de durcissement consistant en un maintien entre 450 et 550°C pendant 1 à 10heures. A noter que, lorsque la température de traitement se situe dans la partie supérieure de la plage de température (500 à 550°C), la ductilité est améliorée et la limite élastique est légèrement abaissée.It is then possible to cut a piece into the strip and to shape this piece, for example by folding, then to carry out thereon a hardening treatment consisting of a holding between 450 and 550 ° C. for 1 to 10 hours. Note that when the processing temperature is in the upper part of the temperature range (500 to 550 ° C), the ductility is improved and the yield strength is lowered slightly.
Le traitement de durcissement peut également être effectué au four à passage à une température comprise entre 600°C et 700°C pendant un temps compris entre 30 secondes et 3 minutes.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.
On obtient ainsi une pièce constituée d'un métal ayant une limite d'élasticité élevée et une tenue à la fatigue excellente.This gives a piece made of a metal having a high yield strength and excellent fatigue resistance.
Pendant le traitement de durcissement ou après celui-ci, la pièce peut être durcie en surface par un traitement de nitruration réalisé par un maintien de quelques heures vers 500°C dans un mélange gazeux réactif riche en azote.During the curing treatment or after this, 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.
Dans une variante, des ébauches de pièces peuvent être découpées dans des bandes laminées à froid d'épaisseur supérieure à l'épaisseur finale voulue pour les pièces. Ces ébauches sont mises en forme, éventuellement soudées, puis laminées à froid jusqu'à l'épaisseur finale de façon à avoir un taux d'écrouissage supérieur à 30% ou mieux supérieur à 40%. Les pièces sont alors recuites dans les mêmes conditions que ce qui vient d'être décrit, de façon à obtenir un grain fin d'indice ASTM supérieur à 8, ou mieux supérieur à 10, puis soumises à un traitement de durcissement comme indiqué ci-dessus. La limite d'élasticité obtenue est élevée et la tenue à la fatigue est excellente.Alternatively, 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.
On peut également fabriquer des pièces par découpage, par exemple par découpage chimique, dans des bandes durcies. L'ensemble du procédé, y compris le traitement thermique de durcissement, est alors appliqué à la bande. Ces pièces sont, par exemple, des grilles support de circuits intégrés.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.
L'acier maraging qu'il est préférable d'utiliser pour obtenir de très bonnes propriétés en fatigue et une limite d'élasticité supérieure à 1850 MPa, contient principalement, en % en poids:
- de 12% à 24,5% de nickel,
- de 2,5% à 12% de molybdène,
- de 4,17% à 20% de cobalt,
- from 12% to 24.5% nickel,
- from 2.5% to 12% molybdenum,
- from 4.17% to 20% cobalt,
Afin d'obtenir un point Ms (température de début de transformation martensitique) voisin de 200°C, les teneurs en nickel et molybdène doivent être telles que 20% ≤ Ni + Mo ≤ 27%, et de préférence telles que 22% ≤ Ni + Mo ≤ 25%.In order to obtain a point Ms (martensitic transformation start temperature) close to 200 ° C., the contents of nickel and molybdenum must be such that 20% ≤ Ni + Mo ≤ 27%, and preferably such that 22% ≤ Ni + Mo ≤ 25%.
Afin d'obtenir une limite d'élasticité, après traitement thermique de durcissement, supérieure à 1850 MPa, les teneurs en cobalt et molybdène doivent être telles que Co x Mo ≥ 50, et de préférence telles que Co x Mo ≥ 70. En effet, plus ce produit est élevé, plus la limite d'élasticité est élevée. Mais, pour obtenir une ductilité suffisante, les teneurs en cobalt et molybdène doivent être telles que Co x Mo ≤ 200, et de préférence telles que Co x Mo ≤ 120. Ces valeurs correspondent respectivement à des limites d'élasticité inférieures à environ 3000 MPa et 2500 MPa.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.
Le molybdène a un effet favorable sur le durcissement par nitruration en surface. Pour obtenir un bon durcissement, la teneur en molybdène doit, de préférence, être supérieure à 4%, et mieux supérieure à 6%. Mais, il est préférable qu'elle reste inférieure à 8% pour limiter les problèmes de ségrégation et pour faciliter les opérations de transformation à chaud ainsi que pour améliorer la ductilité du produit final. Deux plages préférentielles de teneurs en molybdène peuvent être définies:
- 4,17 à 6 % de Mo qui correspond à des produits possédant une très bonne aptitude à la transformation à chaud et à froid ainsi qu un très bon compromis entre limite élastique élevée et bonne ductilité et ténacité.
- 6 à 8 % de Mo qui correspond à des aciers à très haute limite élastique ou plus économiques car de teneur réduite en cobalt.
- 4.17 to 6% Mo which corresponds to products having a very good ability to heat and cold transformation and a very good compromise between high yield strength and good ductility and toughness.
- 6 to 8% of Mo which corresponds to steels with very high elastic limit or more economical because of reduced cobalt content.
En combinant toutes ces conditions, on peut définir les domaines de composition préférentiels suivants pour les éléments principaux:
- 1) afin d'obtenir une limite d'élasticité supérieure à 1850 MPa et une aptitude moyenne au durcissement par nitruration:
- 2) afin d'obtenir une limite d'élasticité supérieure à 1850 MPa et une aptitude forte au durcissement par nitruration:
- 3) afin d'obtenir une limite d'élasticité supérieure à 2000 MPa et un point Ms plus favorable:
- 4) afin d'obtenir une limite d'élasticité supérieure à 2000 MPa et un point Ms plus favorable et une aptitude moyenne au durcissement par nitruration:
- 5) afin d'obtenir une limite d'élasticité supérieure à 2000 MPa et un point Ms plus favorable et une aptitude forte au durcissement par nitruration:
- 1) in order to obtain a yield strength greater than 1850 MPa and an average ability to cure by nitriding:
- 2) in order to obtain a yield strength greater than 1850 MPa and a strong ability to cure by nitriding:
- 3) in order to obtain a yield strength greater than 2000 MPa and a more favorable Ms point:
- 4) in order to obtain a yield strength greater than 2000 MPa and a more favorable Ms point and an average ability to cure by nitriding:
- 5) in order to obtain a yield strength greater than 2000 MPa and a more favorable Ms point and a strong aptitude for hardening by nitriding:
Outre les éléments principaux dont les domaines de composition viennent d'être décrits, les éléments résiduels doivent être contrôlés de façon rigoureuse pour obtenir de bonnes propriétés de ductilité et de résistance à la fatigue. Ces limitations sont notamment :
A titre d'exemple et de comparaison, on a réalisé des bandes en acier maraging de composition :
Ni=18,1% Co=16,2% Mo=5,3% Al=0,020% Ti=0,013% Si=0,03% Mn=0,03% C=0,003% Ca<0,0005% S=0,0007% P=0,002 N=0,0023% O<0,001% H<0,0001%, le reste étant du fer et des impuretés. Ces impuretés sont notamment le cuivre et le chrome dont les teneurs sont : Cu=0,07% et Cr=0,06%.
Le point de transformation martensitique Ms de cette coulée est égal à +195°C.By way of example and comparison, we made maraging steel strips of composition:
Ni = 18.1% Co = 16.2% Mo = 5.3% Al = 0.020% Ti = 0.013% Si = 0.03% Mn = 0.03% C = 0.003% Ca <0.0005% S = 0.0007% P = 0.002 N = 0.0023% O <0.001% H <0.0001%, the remainder being iron and impurities. These impurities are in particular copper and chromium whose contents are: Cu = 0.07% and Cr = 0.06%.
The martensitic transformation point Ms of this casting is equal to + 195 ° C.
Ces bandes ont été laminées à froid jusqu'à l'épaisseur de 0,4mm, avec un taux d'écrouissage final de 70%.These strips were cold-rolled to a thickness of 0.4 mm, with a final hardening rate of 70%.
Une première bande A, donnée à titre d'exemple, a été recuite au four à passage sous hydrogène à 1020°C pendant 1 minute pour obtenir un grain fin d'indice ASTM 11 puis durcie par maintien à 490°C pendant 3 heures.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.
Une deuxième bande B, donné à titre de comparaison, a été recuite au four à passage à 1150°C pendant 1 minute pour obtenir un grain grossier d'indice ASTM 7 puis durcie par maintien à 490°C pendant 3 heures.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.
Des essais comparatifs de tenue en fatigue ont été réalisés avec les bandes A et B par traction ondulée, à 25 hertz, avec une contrainte maximale de 750 MPa et une contrainte minimale de 75 MPa.Comparative tests of fatigue strength were carried out with the bands A and B by undulating traction, at 25 hertz, with a maximum stress of 750 MPa and a minimum stress of 75 MPa.
Pour la bande A conforme à l'invention, la limite de fatigue a été supérieure à 8 x 108 cycles, alors que pour la bande B, la limite de fatigue était égale à 5 x 108 cycles. Ces résultats montrent l'intérêt d'un grain fin pour améliorer la tenue à la fatigue de ces bandes.For the band A according to the invention, the fatigue limit was greater than 8 × 10 8 cycles, whereas for the band B the fatigue limit was 5 × 10 8 cycles. These results show the interest of a fine grain to improve the fatigue resistance of these bands.
Les bandes A et B avaient toutes les deux une limite d'élasticité supérieure à 1850 MPa.Both bands A and B had a yield strength greater than 1850 MPa.
Afin de mettre en évidence l'intérêt particulier de la composition chimique préférentielle de l'acier maraging conformément à l'invention, on a également fabriqué une bande en acier maraging contenant 18% de nickel, 9% de cobalt, 5% de molybdène, 0,5% de titane et 0,1% d'aluminium. Cette bande a été fabriquée par le procédé selon l'invention, le grain avait un indice ASTM de 10 et la limite d'élasticité était de 1910 MPa. La limite de fatigue mesurée dans les mêmes conditions d'essai que dans le cas précédent était de 2 x 108 cycles.In order to demonstrate the particular interest of the preferred chemical composition of maraging steel in accordance with the invention, 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.
Ces bandes peuvent avantageusement être utilisées pour fabriquer des courroies ou tout autre produit, tel que des grilles support de circuits intégrés.These strips can advantageously be used to manufacture belts or any other product, such as integrated circuit support grids.
A titre d'exemple, avec des bandes conformes à l'invention on a fabriqué des courroies de transmission pour moteur à combustion interne constituées de cavaliers maintenus par des anneaux constitués de bandes étroites conformes à l'invention et dont les deux extrémités sont soudées. Ces courroies ont une durée de vie plus de dix fois supérieure à la durée de vie de courroies identiques mais fabriquées avec des bandes en acier maraging conforme à l'art antérieur.By way of example, with belts in accordance with the invention, 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.
Claims (10)
- Process for the manufacture of a strip or of a part cut from a strip made of cold-rolled maraging steel hardened by a hardening heat treatment, characterized in that, before the hardening heat treatment is carried out, the strip or the part undergoes cold plastic deformation with a reduction ratio of greater than 30% and the strip or the part undergoes recrystallization annealing so as to obtain a fine grain corresponding to an ASTM index of greater than 8, the chemical composition of the steel comprising, in % by weight:
- Process according to Claim 1, characterized in that, after the recrystallization annealing, the strip or the part undergoes cold rolling with a reduction ratio of between 1% and 10%.
- Process according to Claim 1 or Claim 2, characterized in that the maraging steel is vacuum-remelted by the VAR process or is remelted a first time in a vacuum by the VAR process or electroslag-remelted by the ESR process and remelted a second time in a vacuum by the VAR process.
- Process according to any one of Claims 1 to 3, characterized in that the hardening heat treatment consists of a soak between 450°C and 550°C for 1 to 10 hours.
- Process according to Claim 4, characterized in that, during the hardening heat treatment or after it, the surface of the part is hardened by nitriding.
- Process according to any one of Claims 1 to 3, characterized in that the hardening heat treatment is carried out in a continuous furnace at a temperature of between 600°C and 700°C for a time of between 30 seconds and 3 minutes.
- Process according to Claim 6, characterized in that after the hardening heat treatment the surface of the part is hardened by nitriding.
- Strip or part, having a thickness of less than 1 mm, made of maraging steel, characterized in that the steel of which the strip or part is made has a fine grain corresponding to an ASTM index of greater than 8 and in that the composition of the steel comprises, in % by weight:
- Transmission belt comprising at least one strip or part according to Claim 8.
- Leadframe for integrated circuits, consisting of a part according to Claim 1.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
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CY20071101302T CY1106925T1 (en) | 2000-11-17 | 2007-09-10 | PROCEDURE FOR CONSTRUCTION OF A TAPE OR A PIECE CUT BY A STEEL COOLING TAPE STAINLESS STEEL |
Applications Claiming Priority (3)
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FR0014807 | 2000-11-17 | ||
FR0014807A FR2816959B1 (en) | 2000-11-17 | 2000-11-17 | PROCESS FOR MANUFACTURING A STRIP OR A CUT PIECE IN A COLD-ROLLED MARAGING STEEL STRIP |
PCT/FR2001/003595 WO2002040722A1 (en) | 2000-11-17 | 2001-11-16 | Method for making a strip or a workpiece cut out from a cold rolled maraging steel strip |
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EP1339880B1 true EP1339880B1 (en) | 2007-07-11 |
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US (1) | US6663730B2 (en) |
EP (1) | EP1339880B1 (en) |
JP (2) | JP4278378B2 (en) |
KR (2) | KR100884639B1 (en) |
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WO2017064537A1 (en) | 2015-10-15 | 2017-04-20 | Aperam | Steel, product created from said steel, and manufacturing method thereof |
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2001
- 2001-11-16 WO PCT/FR2001/003595 patent/WO2002040722A1/en active IP Right Grant
- 2001-11-16 KR KR1020037006549A patent/KR100884639B1/en active IP Right Grant
- 2001-11-16 ES ES01996631T patent/ES2287187T3/en not_active Expired - Lifetime
- 2001-11-16 DE DE60129350T patent/DE60129350T2/en not_active Expired - Lifetime
- 2001-11-16 PT PT01996631T patent/PT1339880E/en unknown
- 2001-11-16 DK DK01996631T patent/DK1339880T3/en active
- 2001-11-16 EP EP01996631A patent/EP1339880B1/en not_active Expired - Lifetime
- 2001-11-16 AR ARP010105379A patent/AR034276A1/en unknown
- 2001-11-16 TW TW090128454A patent/TW539746B/en active
- 2001-11-16 KR KR1020087009332A patent/KR20080048544A/en not_active Application Discontinuation
- 2001-11-16 AU AU2002218382A patent/AU2002218382A1/en not_active Abandoned
- 2001-11-16 AT AT01996631T patent/ATE366826T1/en active
- 2001-11-16 CN CNB018188265A patent/CN1298869C/en not_active Expired - Lifetime
- 2001-11-16 JP JP2002543031A patent/JP4278378B2/en not_active Expired - Lifetime
- 2001-11-19 US US09/988,134 patent/US6663730B2/en not_active Expired - Lifetime
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2007
- 2007-09-10 CY CY20071101302T patent/CY1106925T1/en unknown
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2008
- 2008-04-25 JP JP2008115217A patent/JP4965502B2/en not_active Expired - Lifetime
Non-Patent Citations (1)
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Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016170397A1 (en) | 2015-04-23 | 2016-10-27 | Aperam | Steel, product made of said steel, and manufacturing method thereof |
WO2016170519A1 (en) | 2015-04-23 | 2016-10-27 | Aperam | Steel, product made of said steel, and manufacturing method thereof |
WO2017064537A1 (en) | 2015-10-15 | 2017-04-20 | Aperam | Steel, product created from said steel, and manufacturing method thereof |
WO2017064684A1 (en) | 2015-10-15 | 2017-04-20 | Aperam | Steel, product created from said steel, and manufacturing method thereof |
CN108138286A (en) * | 2015-10-15 | 2018-06-08 | 艾普伦 | Steel, the product of the steel making and its manufacturing method |
US10731231B2 (en) | 2015-10-15 | 2020-08-04 | Aperam | Steel, product created from said steel, and manufacturing method thereof |
CN116024505A (en) * | 2015-10-15 | 2023-04-28 | 艾普伦 | Steel, product made of said steel and method for manufacturing same |
Also Published As
Publication number | Publication date |
---|---|
JP4965502B2 (en) | 2012-07-04 |
FR2816959A1 (en) | 2002-05-24 |
CY1106925T1 (en) | 2012-09-26 |
US20020059967A1 (en) | 2002-05-23 |
ATE366826T1 (en) | 2007-08-15 |
WO2002040722A1 (en) | 2002-05-23 |
TW539746B (en) | 2003-07-01 |
US6663730B2 (en) | 2003-12-16 |
AU2002218382A1 (en) | 2002-05-27 |
KR20080048544A (en) | 2008-06-02 |
JP2004514056A (en) | 2004-05-13 |
CN1298869C (en) | 2007-02-07 |
PT1339880E (en) | 2007-08-13 |
KR100884639B1 (en) | 2009-02-23 |
KR20030055303A (en) | 2003-07-02 |
EP1339880A1 (en) | 2003-09-03 |
ES2287187T3 (en) | 2007-12-16 |
DE60129350D1 (en) | 2007-08-23 |
JP2008274436A (en) | 2008-11-13 |
FR2816959B1 (en) | 2003-08-01 |
AR034276A1 (en) | 2004-02-18 |
DK1339880T3 (en) | 2007-09-10 |
JP4278378B2 (en) | 2009-06-10 |
CN1630732A (en) | 2005-06-22 |
DE60129350T2 (en) | 2008-03-13 |
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