EP0787812A1 - Steel for the manufacture of forgings and process for manufacturing said forgings - Google Patents
Steel for the manufacture of forgings and process for manufacturing said forgings Download PDFInfo
- Publication number
- EP0787812A1 EP0787812A1 EP97400025A EP97400025A EP0787812A1 EP 0787812 A1 EP0787812 A1 EP 0787812A1 EP 97400025 A EP97400025 A EP 97400025A EP 97400025 A EP97400025 A EP 97400025A EP 0787812 A1 EP0787812 A1 EP 0787812A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- optionally
- steel
- temperature
- process according
- possibly
- 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.)
- Granted
Links
Classifications
-
- 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
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
-
- 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
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Definitions
- the present invention relates to the manufacture of forgings with high characteristics, made of steel.
- the parts are made of a steel of the chromium-molybdenum type, the chemical composition of which comprises, by weight, from 0.25% to 0.45% of carbon, approximately 1% of chromium and approximately 0, 25% molybdenum.
- the parts are forged and then subjected to a quenching and tempering heat treatment intended to give them a tempered martensitic structure in order to obtain in particular a tensile strength Rm of the order of 1000 MPa.
- This technique has the disadvantage of being costly and sometimes of causing distortions in the geometry of the parts.
- the forgings can also be made of steel containing less carbon than in the previous case, and be soaked in water in the hot forging to give them a bainitic or bainito-martensitic structure.
- This technique makes it possible to obtain a tensile strength Rm greater than 1000 MPa and an elastic limit Rp 0.2 greater than 800 MPa, but it has the drawback of requiring water quenching which, sometimes generates geometrical deformations imposing the need for a straightening operation or which can even be prohibitive.
- Some parts finally, are made of steel containing between 0.3% and 0.4% carbon and between 1.9% and 2.5% manganese. They are air-cooled after forging so as to present a bainitic structure with high mechanical characteristics. However, these parts often have segregated bands with martensitic structure making machining difficult.
- the object of the present invention is to provide a steel and a method for the manufacture of forgings with high characteristics which remedy these drawbacks.
- the carbon content is less than or equal to 0.3%, preferably also, the manganese content is less than 1.6%.
- the silicon content may preferably be either greater than 1.2% or less than 0.8%.
- the cooling rate Vr is greater than 2 ° C / s.
- the part After maintaining between Tm and Tf, the part can be cooled to room temperature and, optionally, be subjected to tempering between 150 ° C and 650 ° C.
- the part After holding between Tm and Tf, the part can also be reheated to a temperature below 650 ° C, then cooled to room temperature.
- the heat treatment can be carried out either after heating the part to a temperature above AC 3 , or directly after forging.
- a piece of steel is supplied according to the invention and it is hot forged after having heated it to a temperature above AC 3, preferably above 1150 ° C., and better still, between 1200 ° C and 1280 ° C, so as to have given it an entirely austenitic structure and a sufficiently low flow stress.
- the part is subjected to a heat treatment which can be carried out either directly in the hot forging, or after cooling of the part and reheating above the temperature AC 3 of the steel.
- the heat treatment comprises cooling at a cooling rate Vr measured at the passage at 700 ° C greater than 0.5 ° C / s, and preferably greater than 2 ° C / s, to a temperature Tm between Ms + 100 ° C and Ms-20 ° C, Ms being the temperature at the start of martensitic transformation of the steel.
- This cooling is followed by holding for a time greater than 2 min between the temperature Tm and a temperature Tf ⁇ Tm-100 ° C, and preferably Tf ⁇ Tm-60 ° C. Maintaining is followed either by cooling to ambient temperature possibly supplemented by tempering between 150 ° C and 650 ° C, or by reheating to a temperature less than or equal to 650 ° C before cooling to at room temperature.
- the purpose of this heat treatment is to give the part an essentially bainitic structure comprising less than 20% of ferrite and at least 15%, and preferably at least 30%, of lower bainite formed between Tm and Tf. he can be carried out on the whole part or simply on a part having a particular functionality.
- Tm, Tf, duration The conditions of maintenance (Tm, Tf, duration), as well as the proportions of each of the structures, and in particular the proportion of lower bainite, can be determined, in a manner known to those skilled in the art, using measurements. dilatometric on test bars.
- the parts thus obtained have the advantage of having a tensile strength Rm of between 950 MPa and 1150 MPa, an elastic limit Rp 0.2 greater than 750 MPa, a Mesnager K resilience greater than 25 Joules / Cm 2 to 20 ° C, machinability at least equal to that of parts having a ferrito-pearlitic structure and good fatigue strength: ⁇ D / Rm> 0.5 in rotary bending at 2x10 6 cycles.
- an axle was manufactured with a steel whose chemical composition included, in% by weight: VS Yes Mn Or Cr Mo Cu V Al B Ti Nb 0.25 0.5 1.67 0.09 0.52 - 0.199 0.2 0.03 - 0.02 - this steel also contained 0.065% S to improve machinability. Its Ms temperature was 380 ° C.
- the part was hot forged between 1280 ° C and 1050 ° C. Directly after forging, the part was cooled with blown air at the speed of 2.6 ° C / s to the temperature of 425 ° C, then kept between 425 ° C and 400 ° C for 10 min; finally, the part was cooled to room temperature by natural air cooling.
- a rocket was made with a steel whose chemical composition included, in% by weight: VS Yes Mn Or Cr Mo Cu V Al B Ti Nb 0.25 0.5 1.63 0.006 0.51 0.09 0.196 0.107 0.038 0.003 0.023 - this steel also contained 0.05% S to improve machinability. Its Ms temperature was 385 ° C.
- the part was hot forged between 1270 ° C and 1040 ° C. Directly after forging, the part was cooled with blown air at a speed of 2.6 ° C / s to a temperature of 400 ° C, then kept between 400 ° C and 380 ° C for 10 minutes; the the part was then brought to the temperature of 550 ° C. for 1 hour, then it was cooled to ambient temperature by natural air cooling.
- a ball joint was made with a steel whose chemical composition included, in% by weight: VS Yes Mn Or Cr Mo Cu V Al B Ti Nb 0.28 0.79 1.63 0.05 0.5 0.09 0.19 - 0.04 0.0033 0.023 - this steel also contained 0.06% S to improve machinability. Its Ms temperature was 350 ° C.
- the part was hot forged between 1270 ° C and 1060 ° C. Directly after forging, the part was cooled in still air at the speed of 1.19 ° C / s to the temperature of 380 ° C, then kept between 380 ° C and 360 ° C for 10 min; finally, the part was cooled to room temperature by natural air cooling.
- the parts thus obtained can be in particular parts for the automobile such as suspension wishbones, transmission shafts, connecting rods, but they can also be shafts, cams or any other forged part for various machines.
Abstract
Description
La présente invention est relative à la fabrication de pièces forgées à hautes caractéristiques, en acier.The present invention relates to the manufacture of forgings with high characteristics, made of steel.
Les pièces forgées à hautes caractéristiques, en acier, et notamment les pièces forgées à hautes caractéristiques pour l'automobile, sont fabriquées selon différentes techniques qui présentent chacune des inconvénients.Steel forgings with high characteristics, and in particular forgings with high characteristics for the automobile, are manufactured according to different techniques which each have drawbacks.
Selon une première technique, les pièces sont constituées d'un acier du type chrome-molybdène, dont la composition chimique comprend, en poids, de 0,25 % à 0,45 % de carbone, environ 1 % de chrome et environ 0,25 % de molybdène. Les pièces sont forgées puis soumises à un traitement thermique de trempe et de revenu destiné à leur conférer une structure martensitique revenue pour obtenir notamment une résistance à la traction Rm de l'ordre de 1000 MPa. Cette technique présente l'inconvénient d'être coûteuse et d'engendrer parfois des déformations de la géométrie des pièces.According to a first technique, the parts are made of a steel of the chromium-molybdenum type, the chemical composition of which comprises, by weight, from 0.25% to 0.45% of carbon, approximately 1% of chromium and approximately 0, 25% molybdenum. The parts are forged and then subjected to a quenching and tempering heat treatment intended to give them a tempered martensitic structure in order to obtain in particular a tensile strength Rm of the order of 1000 MPa. This technique has the disadvantage of being costly and sometimes of causing distortions in the geometry of the parts.
Selon une autre technique, les pièces sont constituées d'un acier contenant de 0,3% à 0,4% de carbone, de 1% à 1,7% de manganèse, de 0,25% à 1% de silicium et jusqu'à 0,1% de vanadium. Après forgeage, les pièces sont refroidies lentement pour leur conférer une structure ferrito-perlitique. Cette technique moins coûteuse que la précédente a cependant plusieurs inconvénients:
- il n'est pas possible d'obtenir une résistance à la traction Rm supérieure à 1000 MPa,
- le rapport limite d'élasticité sur résistance à la traction Rp0,2/Rm est inférieur à 0,75 ce qui limite les possibilités d'allégement des pièces lorsque celles-ci sont dimensionnées en particulier par référence à la limite d'élasticité,
- la température de transition de la résilience est supérieure à 50°C ce qui conduit à une résistance aux chocs faible,
- il est parfois nécessaire d'adapter les installations de fabrication en ajoutant des tunnels de refroidissement pour obtenir un refroidissement adapté après forgeage.
- it is not possible to obtain a tensile strength Rm greater than 1000 MPa,
- the elasticity limit to tensile strength ratio Rp 0.2 / Rm is less than 0.75, which limits the possibilities of lightening the parts when they are dimensioned in particular by reference to the elasticity limit,
- the resilience transition temperature is greater than 50 ° C., which leads to low impact resistance,
- it is sometimes necessary to adapt the manufacturing facilities by adding cooling tunnels to obtain suitable cooling after forging.
Les pièces forgée peuvent également être constituées d'un acier contenant moins de carbone que dans le cas précédant, et être trempées à l'eau dans la chaude de forgeage pour leur conférer une structure bainitique ou bainito-martensitique. Cette technique permet d'obtenir une résistance à la traction Rm supérieure à 1000 MPa et une limite d'élasticité Rp0,2 supérieure à 800 MPa, mais elle présente l'inconvénient d'exiger une trempe à l'eau qui, parfois, engendre des déformations géométriques imposant la nécessité d'une opération de redressage ou qui peuvent, même, être rédhibitoires.The forgings can also be made of steel containing less carbon than in the previous case, and be soaked in water in the hot forging to give them a bainitic or bainito-martensitic structure. This technique makes it possible to obtain a tensile strength Rm greater than 1000 MPa and an elastic limit Rp 0.2 greater than 800 MPa, but it has the drawback of requiring water quenching which, sometimes generates geometrical deformations imposing the need for a straightening operation or which can even be prohibitive.
Certaines pièces, enfin, sont constituées d'un acier contenant entre 0,3% et 0,4% de carbone et entre 1,9% et 2,5% de manganèse. Elles sont refroidies à l'air après forgeage de façon à présenter une structure bainitique à caractéristiques mécaniques élevées. Mais, ces pièces comportent souvent des bandes ségrégées à structure martensitique rendant l'usinage difficile.Some parts, finally, are made of steel containing between 0.3% and 0.4% carbon and between 1.9% and 2.5% manganese. They are air-cooled after forging so as to present a bainitic structure with high mechanical characteristics. However, these parts often have segregated bands with martensitic structure making machining difficult.
Le but de la présente invention est de proposer un acier et un procédé pour la fabrication de pièces forgées à hautes caractéristiques qui remédient à ces inconvénients.The object of the present invention is to provide a steel and a method for the manufacture of forgings with high characteristics which remedy these drawbacks.
A cet effet, l'invention a pour objet un acier pour la fabrication de pièces forgées dont la composition chimique comprend, en poids:
- éventuellement de 0,005% à 0,06% d'aluminium,
- éventuellement du bore en des teneurs comprises entre 0,0005% et 0,01%,
- éventuellement entre 0,005% et 0,03% de titane,
- éventuellement entre 0,005% et 0,06% de niobium,
- éventuellement de 0,005% à 0,1% de soufre, éventuellement jusqu'à 0,006% de calcium, éventuellement jusqu'à 0,03% de tellure, éventuellement jusqu'à 0,05% de sélénium, éventuellement jusqu'à 0,05% de bismuth, éventuellement jusqu'à 0,1% de plomb,
le reste étant du fer et des impuretés résultant de l'élaboration.
- optionally from 0.005% to 0.06% aluminum,
- optionally boron in contents of between 0.0005% and 0.01%,
- optionally between 0.005% and 0.03% of titanium,
- optionally between 0.005% and 0.06% niobium,
- optionally from 0.005% to 0.1% sulfur, optionally up to 0.006% calcium, optionally up to 0.03% tellurium, optionally up to 0.05% selenium, optionally up to 0.05 % bismuth, possibly up to 0.1% lead,
the remainder being iron and impurities resulting from processing.
De préférence, la teneur en carbone est inférieure ou égale à 0,3%, de préférence également, la teneur en manganèse est inférieure à 1,6%. Selon la nature des applications envisagées, la teneur en silicium peut être, de préférence, soit supérieure à 1,2% soit inférieure à 0,8%.Preferably, the carbon content is less than or equal to 0.3%, preferably also, the manganese content is less than 1.6%. Depending on the nature of the applications envisaged, the silicon content may preferably be either greater than 1.2% or less than 0.8%.
L'invention concerne également un procédé pour la fabrication d'une pièce forgée selon lequel:
- on approvisionne un lopin en un acier selon l'invention et on le forge à chaud pour obtenir une pièce,
- on soumet la pièce à un traitement thermique comportant un refroidissement depuis une température à la quelle l'acier est entièrement austénitique jusqu'à une température Tm comprise entre Ms+100°C et Ms-20°C à une vitesse de refroidissement Vr supérieure à 0,5°C/s, suivi d'un maintien de la pièce entre Tm et Tf, avec Tf ≥ Tm-100°C, et de préférence Tf ≥ Tm-60°C, pendant au moins 2 minutes de façon à obtenir une structure comportant au moins 15%, et de préférence, au moins 30% de bainite formée entre Tm et Tf.
- a piece of steel is supplied according to the invention and it is hot forged to obtain a part,
- the part is subjected to a heat treatment comprising cooling from a temperature at which the steel is entirely austenitic up to a temperature Tm of between Ms + 100 ° C and Ms-20 ° C at a cooling rate Vr greater than 0.5 ° C / s, followed by holding the part between Tm and Tf, with Tf ≥ Tm-100 ° C, and preferably Tf ≥ Tm-60 ° C, for at least 2 minutes so as to obtain a structure comprising at least 15%, and preferably, at least 30% of bainite formed between Tm and Tf.
De préférence, la vitesse de refroidissement Vr est supérieure à 2°C/s.Preferably, the cooling rate Vr is greater than 2 ° C / s.
Après le maintien entre Tm et Tf, la pièce peut être refroidie jusqu'à la température ambiante et, éventuellement, être soumise à .un revenu entre 150°C et 650°C.After maintaining between Tm and Tf, the part can be cooled to room temperature and, optionally, be subjected to tempering between 150 ° C and 650 ° C.
Après le maintien entre Tm et Tf, la pièce peut, également, être réchauffée à une température inférieure à 650°C, puis refroidie jusqu'à la température ambiante.After holding between Tm and Tf, the part can also be reheated to a temperature below 650 ° C, then cooled to room temperature.
Le traitement thermique peut être effectué soit après un chauffage de la pièce à une température supérieure à AC3, soit directement après forgeage.The heat treatment can be carried out either after heating the part to a temperature above AC 3 , or directly after forging.
L'invention va maintenant être décrite de façon plus précise, mais non limitative et illustrée par les exemples qui suivent.The invention will now be described in more detail, but without limitation, and illustrated by the examples which follow.
La composition chimique de l'acier selon l'invention comprend, en poids:
- plus de 0,1% de carbone, et de préférence plus de 0,15%, pour obtenir une dureté suffisante, mais, moins de 0,4%, et de préférence moins de 0,3 %, afin de limiter la résistance à la traction Rm à 1200 MPa;
- plus de 1% de manganèse pour obtenir une trempabilité suffisante, mais moins de 1,8%, et de préférence moins de 1,6 % pour éviter la formation de bandes ségrégées;
- plus de 0,15% de silicium pour durcir la ferrite et, éventuellement, pour favoriser la formation d'austénite résiduelle ce qui améliore la limite d'endurance en fatigue, mais moins de 1,7%, car, au delà, le silicium fragilise l'acier; entre 0,15 % et 0,8% le silicium durcit la ferrite sans favoriser la formation d'austénite résiduelle; entre 1,2 % et 1,7 % le silicium favorise suffisamment la formation d'austénite résiduelle pour améliorer la limite d'endurance en fatigue; selon les applications, la teneur en silicium peut être choisie dans l'une ou l'autre de ces plages;
- de 0% à 1% de nickel, de 0% à 1,2% de chrome et de 0% à 0,3% de molybdène pour ajuster la trempabilité;
- éventuellement du titane en des teneurs comprises entre 0,005% et 0,03%;
- éventuellement du niobium en des teneurs comprises entre 0,005% et 0,06%;
- éventuellement du bore en des teneurs comprises entre 0,0005 % et 0,01% pour compléter l'effet des élément précédents sur la trempabilité; dans ce cas, il est préférable que l'acier contienne du titane pour renforcer l'effet du bore;
- de 0% à 0,3% de vanadium pour obtenir un durcissement complémentaire et améliorer la trempabilité;
- moins de 0,35% de cuivre, élément résiduel présent fréquemment dans l'acier élaboré à partir de ferrailles, mais qui, en trop grande quantité, a l'inconvénient de détériorer la forgeabilité;
- éventuellement de 0,005% à 0,06% d'aluminium pour assurer la désoxydation de l'acier et pour contrôler le grossissement du grain austénitique, notamment lorsque la teneur en silicium est inférieure à 0,5 %;
- éventuellement de 0,005% à 0,1% de soufre, éventuellement jusqu'à 0,006% de calcium, éventuellement jusqu'à 0,03% de tellure, éventuellement jusqu'à 0,05% de sélénium, éventuellement jusqu'à 0,05% de bismuth, éventuellement jusqu'à 0,1% de plomb, pour améliorer l'usinabilité;
le reste étant du fer et des impuretés résultant de l'élaboration.
- more than 0.1% carbon, and preferably more than 0.15%, to obtain sufficient hardness, but less than 0.4%, and preferably less than 0.3%, in order to limit the resistance to the traction Rm at 1200 MPa;
- more than 1% of manganese to obtain sufficient quenchability, but less than 1.8%, and preferably less than 1.6% to avoid the formation of segregated bands;
- more than 0.15% of silicon to harden the ferrite and, possibly, to favor the formation of residual austenite which improves the limit of endurance in fatigue, but less than 1.7%, because, beyond, silicon weakens steel; between 0.15% and 0.8% the silicon hardens the ferrite without promoting the formation of residual austenite; between 1.2% and 1.7% silicon sufficiently promotes the formation of residual austenite to improve the fatigue endurance limit; depending on the applications, the silicon content can be chosen from one or other of these ranges;
- from 0% to 1% nickel, from 0% to 1.2% chromium and from 0% to 0.3% molybdenum to adjust the hardenability;
- optionally titanium in contents of between 0.005% and 0.03%;
- optionally niobium in contents of between 0.005% and 0.06%;
- optionally boron in contents of between 0.0005% and 0.01% to complete the effect of the preceding elements on the quenchability; in this case, it is preferable that the steel contains titanium to enhance the effect of boron;
- from 0% to 0.3% vanadium to obtain additional hardening and improve the hardenability;
- less than 0.35% copper, a residual element frequently present in steel produced from scrap, but which, in too large a quantity, has the disadvantage of deteriorating the forgeability;
- optionally from 0.005% to 0.06% of aluminum to ensure the deoxidation of the steel and to control the magnification of the austenitic grain, in particular when the silicon content is less than 0.5%;
- optionally from 0.005% to 0.1% sulfur, optionally up to 0.006% calcium, optionally up to 0.03% tellurium, optionally up to 0.05% selenium, optionally up to 0.05 % bismuth, possibly up to 0.1% lead, to improve machinability;
the remainder being iron and impurities resulting from processing.
Pour fabriquer une pièce forgée, on approvisionne un lopin en acier selon l'invention et on le forge à chaud après l'avoir chauffé à une température supérieure à AC3, de préférence supérieure à 1150 °C, et mieux encore, comprise entre 1200°C et 1280 °C, de façon à lui avoir conféré une structure entièrement austénitique et une contrainte d'écoulement suffisamment faible. Après forgeage, on soumet la pièce à un traitement thermique qui peut être effectué soit directement dans la chaude de forgeage, soit après refroidissement de la pièce et réchauffage au dessus de la température AC3 de l'acier.To manufacture a forged part, a piece of steel is supplied according to the invention and it is hot forged after having heated it to a temperature above AC 3, preferably above 1150 ° C., and better still, between 1200 ° C and 1280 ° C, so as to have given it an entirely austenitic structure and a sufficiently low flow stress. After forging, the part is subjected to a heat treatment which can be carried out either directly in the hot forging, or after cooling of the part and reheating above the temperature AC 3 of the steel.
Le traitement thermique comporte un refroidissement à une vitesse de refroidissement Vr mesurée au passage à 700 °C supérieure à 0,5°C/s, et de préférence supérieure à 2 °C/s, jusqu'à une température Tm comprise entre Ms+100°C et Ms-20°C, Ms étant la température de début de transformation martensitique de l'acier. Ce refroidissement est suivi par un maintien pendant un temps supérieur à 2 mn entre la température Tm et une température Tf ≥ Tm-100°C, et de préférence Tf ≥ Tm-60°C. Le maintien est suivi soit d'un refroidissement jusqu'à la température ambiante éventuellement complété par un revenu entre 150 °C et 650 °C, soit d'un réchauffage jusqu'à une température inférieure ou égale à 650°C avant refroidissement jusqu'à la température ambiante.The heat treatment comprises cooling at a cooling rate Vr measured at the passage at 700 ° C greater than 0.5 ° C / s, and preferably greater than 2 ° C / s, to a temperature Tm between Ms + 100 ° C and Ms-20 ° C, Ms being the temperature at the start of martensitic transformation of the steel. This cooling is followed by holding for a time greater than 2 min between the temperature Tm and a temperature Tf ≥ Tm-100 ° C, and preferably Tf ≥ Tm-60 ° C. Maintaining is followed either by cooling to ambient temperature possibly supplemented by tempering between 150 ° C and 650 ° C, or by reheating to a temperature less than or equal to 650 ° C before cooling to at room temperature.
Ce traitement thermique a pour but de conférer à la pièce une structure essentiellement bainitique comportant moins de 20% de ferrite et au moins 15%, et de préférence au moins 30 %, de bainite inférieure formée entre Tm et Tf. Il peut être effectué sur toute la pièce ou simplement sur une partie ayant une fonctionnalité particulière.The purpose of this heat treatment is to give the part an essentially bainitic structure comprising less than 20% of ferrite and at least 15%, and preferably at least 30%, of lower bainite formed between Tm and Tf. he can be carried out on the whole part or simply on a part having a particular functionality.
Les conditions du maintien (Tm, Tf, durée), ainsi que les proportions de chacune des structures, et en particulier la proportion de bainite inférieure, peuvent être déterminées, de façon connue par l'Homme du Métier, à l'aide de mesures dilatométriques sur des barreaux d'essai.The conditions of maintenance (Tm, Tf, duration), as well as the proportions of each of the structures, and in particular the proportion of lower bainite, can be determined, in a manner known to those skilled in the art, using measurements. dilatometric on test bars.
Les pièces ainsi obtenues ont l'avantage d'avoir une résistance à la traction Rm comprise entre 950 MPa et 1150 MPa, une limite d'élasticité Rp0.2 supérieure à 750 MPa, une résilience Mesnager K supérieure à 25 Joules/Cm2 à 20°C, une usinabilité au moins égale à celle des pièces ayant une structure ferrito-perlitique et une bonne tenue en fatigue : σD / Rm > 0,5 en flexion rotative à 2x106 cycles.The parts thus obtained have the advantage of having a tensile strength Rm of between 950 MPa and 1150 MPa, an elastic limit Rp 0.2 greater than 750 MPa, a Mesnager K resilience greater than 25 Joules / Cm 2 to 20 ° C, machinability at least equal to that of parts having a ferrito-pearlitic structure and good fatigue strength: σ D / Rm> 0.5 in rotary bending at 2x10 6 cycles.
A titre de premier exemple, on a fabriqué un axe avec un acier dont la composition chimique comportait, en % en poids:
La pièce a été forgée à chaud entre 1280°C et 1050°C. Directement après forgeage, la pièce a été refroidie à l'air soufflé à la vitesse de 2,6°C/s jusqu'à la température de 425°C, puis maintenue entre 425°C et 400°C pendant 10 mn; enfin, la pièce a été refroidie jusqu'à la température ambiante par refroidissement naturel à l'air.The part was hot forged between 1280 ° C and 1050 ° C. Directly after forging, the part was cooled with blown air at the speed of 2.6 ° C / s to the temperature of 425 ° C, then kept between 425 ° C and 400 ° C for 10 min; finally, the part was cooled to room temperature by natural air cooling.
La pièce ainsi obtenue avait une structure comportant au moins 80% de bainite. Ses caractéristiques étaient:
A titre de deuxième exemple, on a fabriqué une fusée avec un acier dont la composition chimique comportait, en % en poids:
La pièce a été forgée à chaud entre 1270°C et 1040°C. Directement après forgeage, la pièce a été refroidie à l'air soufflé à la vitesse de 2,6°C/s jusqu'à la température de 400°C, puis maintenue entre 400°C et 380°C pendant 10 mn; la pièce a alors été portée à la température de 550°C pendant 1 heure, puis elle a été refroidie jusqu'à la température ambiante par refroidissement naturel à l'air.The part was hot forged between 1270 ° C and 1040 ° C. Directly after forging, the part was cooled with blown air at a speed of 2.6 ° C / s to a temperature of 400 ° C, then kept between 400 ° C and 380 ° C for 10 minutes; the the part was then brought to the temperature of 550 ° C. for 1 hour, then it was cooled to ambient temperature by natural air cooling.
La pièce ainsi obtenue avait une structure comportant au moins 80% de bainite. Ses caractéristiques étaient:
A titre de troisième exemple, on a fabriqué une rotule avec un acier dont la composition chimique comportait, en % en poids:
La pièce a été forgée à chaud entre 1270°C et 1060°C. Directement après forgeage, la pièce a été refroidie à l'air calme à la vitesse de 1,19°C/s jusqu'à la température de 380°C, puis maintenue entre 380°C et 360°C pendant 10 mn; enfin, la pièce a été refroidie jusqu'à la température ambiante par refroidissement naturel à l'air.The part was hot forged between 1270 ° C and 1060 ° C. Directly after forging, the part was cooled in still air at the speed of 1.19 ° C / s to the temperature of 380 ° C, then kept between 380 ° C and 360 ° C for 10 min; finally, the part was cooled to room temperature by natural air cooling.
La pièce ainsi obtenue avait une structure comportant au moins 80% de bainite. Ses caractéristiques étaient:
Les pièces ainsi obtenues peuvent être notamment des pièces pour l'automobile telles que des triangles de suspension, des arbres de transmission, des bielles, mais elles peuvent également être des arbres, des cames ou toute autre pièce forgée pour des machines diverses.The parts thus obtained can be in particular parts for the automobile such as suspension wishbones, transmission shafts, connecting rods, but they can also be shafts, cams or any other forged part for various machines.
Claims (14)
le reste étant du fer et des impuretés résultant de l'élaboration.
the remainder being iron and impurities resulting from processing.
le reste étant du fer et des impuretés résultant de l'élaboration.
the remainder being iron and impurities resulting from processing.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9601525A FR2744733B1 (en) | 1996-02-08 | 1996-02-08 | STEEL FOR MANUFACTURING FORGED PART AND METHOD FOR MANUFACTURING FORGED PART |
FR9601525 | 1996-02-08 |
Publications (2)
Publication Number | Publication Date |
---|---|
EP0787812A1 true EP0787812A1 (en) | 1997-08-06 |
EP0787812B1 EP0787812B1 (en) | 2004-03-17 |
Family
ID=9488967
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP97400025A Expired - Lifetime EP0787812B1 (en) | 1996-02-08 | 1997-01-08 | Process for manufacturing steel forging |
Country Status (18)
Country | Link |
---|---|
US (1) | US5820706A (en) |
EP (1) | EP0787812B1 (en) |
JP (1) | JP3915043B2 (en) |
KR (1) | KR970062058A (en) |
AR (1) | AR005719A1 (en) |
AT (1) | ATE262047T1 (en) |
BR (1) | BR9700917A (en) |
CA (1) | CA2196029A1 (en) |
CZ (1) | CZ293691B6 (en) |
DE (1) | DE69728076T2 (en) |
DK (1) | DK0787812T3 (en) |
ES (1) | ES2217374T3 (en) |
FR (1) | FR2744733B1 (en) |
HU (1) | HUP9700269A3 (en) |
NO (1) | NO970548L (en) |
PL (1) | PL182920B1 (en) |
PT (1) | PT787812E (en) |
SI (1) | SI9700025B (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1201774A2 (en) * | 2000-10-25 | 2002-05-02 | Gohsyu Corporation | Forging method |
FR2916371A1 (en) * | 2007-05-24 | 2008-11-28 | Fwu Kuang Entpr Co Ltd | Preparing forged parts having a tensile strength and high elongation, comprises forming forged parts from a wire rod, heating forged parts up to a temperature of specified range, and subjecting forged parts to first and second tempering |
WO2009138586A2 (en) * | 2008-05-15 | 2009-11-19 | Arcelormittal Gandrange | Micro-alloyed steel for hot forging parts having high mechanical characteristics |
WO2013117953A1 (en) * | 2012-02-10 | 2013-08-15 | Ascometal | Process for making a steel part, and steel part so obtained |
WO2016151390A1 (en) | 2015-03-23 | 2016-09-29 | Arcelormittal | Parts with a bainitic structure having high strength properties and manufacturing process |
Families Citing this family (23)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3524790B2 (en) * | 1998-09-30 | 2004-05-10 | 株式会社神戸製鋼所 | Coating steel excellent in coating film durability and method for producing the same |
AP2002002553A0 (en) * | 1999-12-23 | 2002-06-30 | Pfizer Prod Inc | Hydrogel-driven Drug Dosoge Form. |
US7416617B2 (en) | 2002-10-01 | 2008-08-26 | Sumitomo Metal Industries, Ltd. | High strength seamless steel pipe excellent in hydrogen-induced cracking resistance |
FR2847910B1 (en) * | 2002-12-03 | 2006-06-02 | Ascometal Sa | METHOD FOR MANUFACTURING A FORGED STEEL PIECE AND PART THUS OBTAINED |
JP4375971B2 (en) * | 2003-01-23 | 2009-12-02 | 大同特殊鋼株式会社 | Steel for high-strength pinion shaft |
AR047467A1 (en) | 2004-01-30 | 2006-01-18 | Sumitomo Metal Ind | STEEL TUBE WITHOUT SEWING FOR OIL WELLS AND PROCEDURE TO MANUFACTURE |
DE602005016522D1 (en) | 2005-03-09 | 2009-10-22 | Ovako Bar Oy Ab | High-strength air-cooled steel and resulting thermoformed product. |
JP3816937B1 (en) * | 2005-03-31 | 2006-08-30 | 株式会社神戸製鋼所 | Steel sheet for hot-formed product, method for producing the same, and hot-formed product |
JP4677868B2 (en) * | 2005-09-26 | 2011-04-27 | 大同特殊鋼株式会社 | Steel that can be welded with high strength and high toughness, and a method for producing a member using the same |
DE102006060994B4 (en) * | 2006-12-20 | 2010-02-11 | Zf Friedrichshafen Ag | Stainless steel ball studs and sleeves |
US9132567B2 (en) | 2007-03-23 | 2015-09-15 | Dayton Progress Corporation | Tools with a thermo-mechanically modified working region and methods of forming such tools |
US8968495B2 (en) * | 2007-03-23 | 2015-03-03 | Dayton Progress Corporation | Methods of thermo-mechanically processing tool steel and tools made from thermo-mechanically processed tool steels |
JP5483859B2 (en) * | 2008-10-31 | 2014-05-07 | 臼井国際産業株式会社 | Processed product of high-strength steel excellent in hardenability and manufacturing method thereof, and manufacturing method of fuel injection pipe and common rail for diesel engine excellent in high strength, impact resistance and internal pressure fatigue resistance |
NL2002248C2 (en) * | 2008-11-24 | 2010-05-26 | Weweler Nv | Hardening of flexible trailing arms. |
DE102009016079B4 (en) | 2009-04-03 | 2018-09-06 | Zf Friedrichshafen Ag | Ball stud made of a steel with a bainitic structure and method for producing such ball studs |
FR2958660B1 (en) | 2010-04-07 | 2013-07-19 | Ascometal Sa | STEEL FOR MECHANICAL PIECES WITH HIGH CHARACTERISTICS AND METHOD FOR MANUFACTURING THE SAME. |
CN102444573A (en) * | 2010-10-11 | 2012-05-09 | 上海腾辉锻造有限公司 | Method for manufacturing forging pump shaft |
ES2391322B1 (en) * | 2011-04-29 | 2013-10-14 | Consejo Superior De Investigaciones Científicas (Csic) | BAINÍTICO STEEL 38MnV6, PROCEDURE OF OBTAINING AND USE. |
US9440693B2 (en) * | 2014-03-20 | 2016-09-13 | Caterpillar Inc. | Air-hardenable bainitic steel part |
FR3022259A1 (en) | 2014-06-16 | 2015-12-18 | Asco Ind | STEEL FOR HIGH PERFORMANCE TREATED SURFACE MECHANICAL PIECES, AND MECHANICAL PIECES THEREOF AND PROCESS FOR PRODUCING SAME |
PT3168312T (en) * | 2015-11-16 | 2019-07-16 | Deutsche Edelstahlwerke Specialty Steel Gmbh & Co Kg | Engineering steel with bainitic structure, forged part produced therefrom and method for making a forged part |
WO2019180492A1 (en) * | 2018-03-23 | 2019-09-26 | Arcelormittal | Forged part of bainitic steel and a method of manufacturing thereof |
FR3123659A1 (en) | 2021-06-02 | 2022-12-09 | Ascometal France Holding Sas | Hot-formed steel part and method of manufacture |
Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DD68973A (en) * | ||||
DE673465C (en) * | 1930-04-01 | 1939-03-22 | August Thyssen Huette Akt Ges | Steel for wear-resistant and tough objects such as rails, wheel tires and toothed wheels |
GB800286A (en) * | 1955-09-13 | 1958-08-20 | United States Steel Corp | Low-alloy high-strength steel |
CS126995B5 (en) * | 1967-01-28 | 1967-09-15 | ||
GB1116160A (en) * | 1965-04-20 | 1968-06-06 | Nippon Kokan Kk | Improvements in or relating to steel alloys |
DE2144325A1 (en) * | 1971-09-03 | 1973-03-15 | Mim Comb Siderurg Galati | Weather resistant constructional steel - is fine grained, weldable and brittle fracture resistant |
SU441335A1 (en) * | 1972-12-26 | 1974-08-30 | Уральский научно-исследовательский институт черных металлов | Steel |
SU602596A1 (en) * | 1976-07-07 | 1978-04-15 | Уральский научно-исследовательский институт черных металлов | Steel for castings |
DE3628712A1 (en) * | 1986-08-23 | 1988-02-25 | Kloeckner Stahl Gmbh | Denitrated, low-alloyed, high-strength fine-grained structural steel |
JPH04141549A (en) * | 1990-09-28 | 1992-05-15 | Aichi Steel Works Ltd | High strength and high toughness non-heat treated steel for hot forging |
JPH06248386A (en) * | 1993-02-26 | 1994-09-06 | Sumitomo Metal Ind Ltd | Steel for machine structure excellent in delayed fracture resistance |
EP0717116A1 (en) * | 1994-12-13 | 1996-06-19 | ASCOMETAL (Société anonyme) | Process for producing a work piece of machine construction steel and work piece produced by this process |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE68973C (en) * | W. ARNEMANN in Hamburg, Büschstr. 13 | Pich machine | ||
FR717116A (en) * | 1930-06-21 | 1932-01-04 | Kraftfahrzeugbedarf Kommandit | Piston for combustion machines |
IT1171403B (en) * | 1981-07-21 | 1987-06-10 | Italtractor | PROCEDURE FOR THE DIRECT HEAT TREATMENT OF LINES FOR TRACTOR CATALOGS OR TRACKED VEHICLES |
JPS6096718A (en) * | 1983-10-31 | 1985-05-30 | Kobe Steel Ltd | Manufacture of steel sheet excellent in resistances to hydrogen inducing cracking and stress corrosion crcking |
DD243982A1 (en) * | 1985-12-06 | 1987-03-18 | Suhl Feinmesszeugfab Veb | DEVICE FOR GENERATING THE MEASURING POWER FOR A MEASURING ELEMENT |
JP3003451B2 (en) * | 1992-03-11 | 2000-01-31 | 日本鋼管株式会社 | Wear-resistant steel with excellent workability and weldability |
JP3139876B2 (en) * | 1993-04-05 | 2001-03-05 | 新日本製鐵株式会社 | Method of manufacturing non-heat treated steel for hot forging and non-heat treated hot forged product, and non-heat treated hot forged product |
-
1996
- 1996-02-08 FR FR9601525A patent/FR2744733B1/en not_active Expired - Lifetime
-
1997
- 1997-01-08 DE DE69728076T patent/DE69728076T2/en not_active Expired - Lifetime
- 1997-01-08 PT PT97400025T patent/PT787812E/en unknown
- 1997-01-08 EP EP97400025A patent/EP0787812B1/en not_active Expired - Lifetime
- 1997-01-08 AT AT97400025T patent/ATE262047T1/en active
- 1997-01-08 ES ES97400025T patent/ES2217374T3/en not_active Expired - Lifetime
- 1997-01-08 DK DK97400025T patent/DK0787812T3/en active
- 1997-01-27 CA CA002196029A patent/CA2196029A1/en not_active Abandoned
- 1997-01-28 HU HU9700269A patent/HUP9700269A3/en unknown
- 1997-02-04 SI SI9700025A patent/SI9700025B/en unknown
- 1997-02-05 AR ARP970100459A patent/AR005719A1/en unknown
- 1997-02-06 KR KR1019970003801A patent/KR970062058A/en not_active Application Discontinuation
- 1997-02-06 NO NO970548A patent/NO970548L/en unknown
- 1997-02-07 BR BR9700917A patent/BR9700917A/en not_active IP Right Cessation
- 1997-02-07 PL PL97318366A patent/PL182920B1/en unknown
- 1997-02-07 CZ CZ1997378A patent/CZ293691B6/en not_active IP Right Cessation
- 1997-02-10 US US08/797,135 patent/US5820706A/en not_active Expired - Lifetime
- 1997-02-10 JP JP04166097A patent/JP3915043B2/en not_active Expired - Fee Related
Patent Citations (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DD68973A (en) * | ||||
DE673465C (en) * | 1930-04-01 | 1939-03-22 | August Thyssen Huette Akt Ges | Steel for wear-resistant and tough objects such as rails, wheel tires and toothed wheels |
GB800286A (en) * | 1955-09-13 | 1958-08-20 | United States Steel Corp | Low-alloy high-strength steel |
GB1116160A (en) * | 1965-04-20 | 1968-06-06 | Nippon Kokan Kk | Improvements in or relating to steel alloys |
CS126995B5 (en) * | 1967-01-28 | 1967-09-15 | ||
DE2144325A1 (en) * | 1971-09-03 | 1973-03-15 | Mim Comb Siderurg Galati | Weather resistant constructional steel - is fine grained, weldable and brittle fracture resistant |
SU441335A1 (en) * | 1972-12-26 | 1974-08-30 | Уральский научно-исследовательский институт черных металлов | Steel |
SU602596A1 (en) * | 1976-07-07 | 1978-04-15 | Уральский научно-исследовательский институт черных металлов | Steel for castings |
DE3628712A1 (en) * | 1986-08-23 | 1988-02-25 | Kloeckner Stahl Gmbh | Denitrated, low-alloyed, high-strength fine-grained structural steel |
JPH04141549A (en) * | 1990-09-28 | 1992-05-15 | Aichi Steel Works Ltd | High strength and high toughness non-heat treated steel for hot forging |
JPH06248386A (en) * | 1993-02-26 | 1994-09-06 | Sumitomo Metal Ind Ltd | Steel for machine structure excellent in delayed fracture resistance |
EP0717116A1 (en) * | 1994-12-13 | 1996-06-19 | ASCOMETAL (Société anonyme) | Process for producing a work piece of machine construction steel and work piece produced by this process |
Non-Patent Citations (2)
Title |
---|
PATENT ABSTRACTS OF JAPAN vol. 16, no. 413 (C - 980) 2 September 1992 (1992-09-02) * |
PATENT ABSTRACTS OF JAPAN vol. 18, no. 647 (C - 1283) 8 December 1994 (1994-12-08) * |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1201774A2 (en) * | 2000-10-25 | 2002-05-02 | Gohsyu Corporation | Forging method |
EP1201774A3 (en) * | 2000-10-25 | 2004-03-17 | Gohsyu Corporation | Forging method |
FR2916371A1 (en) * | 2007-05-24 | 2008-11-28 | Fwu Kuang Entpr Co Ltd | Preparing forged parts having a tensile strength and high elongation, comprises forming forged parts from a wire rod, heating forged parts up to a temperature of specified range, and subjecting forged parts to first and second tempering |
WO2009138586A2 (en) * | 2008-05-15 | 2009-11-19 | Arcelormittal Gandrange | Micro-alloyed steel for hot forging parts having high mechanical characteristics |
FR2931166A1 (en) * | 2008-05-15 | 2009-11-20 | Arcelormittal Gandrange Sa | HOT FORGED STEEL WITH HIGH MECHANICAL CHARACTERISTICS OF THE PARTS PRODUCED |
WO2009138586A3 (en) * | 2008-05-15 | 2010-01-07 | Arcelormittal Gandrange | Micro-alloyed steel for hot forging parts having high mechanical characteristics |
WO2013117953A1 (en) * | 2012-02-10 | 2013-08-15 | Ascometal | Process for making a steel part, and steel part so obtained |
WO2016151390A1 (en) | 2015-03-23 | 2016-09-29 | Arcelormittal | Parts with a bainitic structure having high strength properties and manufacturing process |
WO2016151345A1 (en) | 2015-03-23 | 2016-09-29 | Arcelormittal | Parts with a bainitic structure having high strength properties and manufacturing process |
Also Published As
Publication number | Publication date |
---|---|
AR005719A1 (en) | 1999-07-14 |
NO970548L (en) | 1997-08-11 |
EP0787812B1 (en) | 2004-03-17 |
ES2217374T3 (en) | 2004-11-01 |
DK0787812T3 (en) | 2004-07-26 |
US5820706A (en) | 1998-10-13 |
DE69728076D1 (en) | 2004-04-22 |
PT787812E (en) | 2004-09-30 |
CZ293691B6 (en) | 2004-07-14 |
FR2744733A1 (en) | 1997-08-14 |
FR2744733B1 (en) | 1998-04-24 |
ATE262047T1 (en) | 2004-04-15 |
MX9700924A (en) | 1998-05-31 |
JP3915043B2 (en) | 2007-05-16 |
SI9700025B (en) | 2002-02-28 |
SI9700025A (en) | 1997-10-31 |
PL182920B1 (en) | 2002-04-30 |
JPH09209086A (en) | 1997-08-12 |
BR9700917A (en) | 1998-09-01 |
HUP9700269A2 (en) | 1998-04-28 |
DE69728076T2 (en) | 2004-08-05 |
PL318366A1 (en) | 1997-08-18 |
HUP9700269A3 (en) | 1999-04-28 |
CA2196029A1 (en) | 1997-08-09 |
CZ37897A3 (en) | 1997-08-13 |
NO970548D0 (en) | 1997-02-06 |
KR970062058A (en) | 1997-09-12 |
HU9700269D0 (en) | 1997-03-28 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0787812B1 (en) | Process for manufacturing steel forging | |
JP5614426B2 (en) | Manufacturing method of machine parts | |
JP5486634B2 (en) | Steel for machine structure for cold working and method for producing the same | |
EP0851038B1 (en) | Steel and process for forming a steel article by cold plastic working | |
EP0629714B1 (en) | Martensitic stainless steel with improved machinability | |
WO2015194411A1 (en) | Steel for mechanical structure for cold working, and method for producing same | |
JP5700174B2 (en) | Induction hardening steel | |
EP1051531B1 (en) | Steel and method for making cleavable mechanical parts | |
JP5278660B2 (en) | Manufacturing method of steel parts | |
EP1426452B1 (en) | Manufacturing process of a bainitic steel article | |
JP5111014B2 (en) | Steel for induction-hardened shaft parts and shaft parts | |
JP3915710B2 (en) | Carburized differential gear with excellent low cycle impact fatigue resistance | |
EP2134882B1 (en) | Microalloyed steel with good resistance to hydrogen for the cold-forming of machine parts having high properties | |
JPS6033338A (en) | Steel to be carburized | |
JP2007107029A (en) | Steel material and its production method | |
US20060057419A1 (en) | High-strength steel product excelling in fatigue strength and process for producing the same | |
FR2672904A1 (en) | Nonmagnetic stainless steel based on manganese-chromium, resistant to stress corrosion, process for the manufacture of a nonmagnetic steel rod of great length | |
JP3623313B2 (en) | Carburized gear parts | |
JPH08260039A (en) | Production of carburized and case hardened steel | |
JP2020139185A (en) | Production method of case hardening steel | |
JPS59232252A (en) | Carburizing steel | |
WO2022210124A1 (en) | Steel wire for machine structural component and manufacturing method therefor | |
WO2022210126A1 (en) | Steel wire for machine structural component and manufacturing method thereof | |
JP2018044235A (en) | Steel wire for machine construction component | |
JP2022158882A (en) | Steel wire for machine structural component and its manufacturing method |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
17P | Request for examination filed |
Effective date: 19970823 |
|
17Q | First examination report despatched |
Effective date: 20020528 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
RTI1 | Title (correction) |
Free format text: PROCESS FOR MANUFACTURING STEEL FORGING |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AT BE CH DE DK ES FI FR GB GR IE IT LI LU NL PT SE |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D Free format text: FRENCH |
|
REF | Corresponds to: |
Ref document number: 69728076 Country of ref document: DE Date of ref document: 20040422 Kind code of ref document: P |
|
REG | Reference to a national code |
Ref country code: GR Ref legal event code: EP Ref document number: 20040401172 Country of ref document: GR |
|
GBT | Gb: translation of ep patent filed (gb section 77(6)(a)/1977) |
Effective date: 20040614 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 |
|
REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 20040602 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2217374 Country of ref document: ES Kind code of ref document: T3 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20041220 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: IE Payment date: 20091231 Year of fee payment: 14 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PT Payment date: 20091217 Year of fee payment: 14 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: LU Payment date: 20100212 Year of fee payment: 14 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 20091221 Year of fee payment: 14 |
|
REG | Reference to a national code |
Ref country code: PT Ref legal event code: MM4A Free format text: LAPSE DUE TO NON-PAYMENT OF FEES Effective date: 20110708 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20110708 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20110802 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20110110 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20110108 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FI Payment date: 20141217 Year of fee payment: 19 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: TP Owner name: ASCO INDUSTRIES, FR Effective date: 20141222 Ref country code: FR Ref legal event code: GC Effective date: 20141222 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: CH Payment date: 20150121 Year of fee payment: 19 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: BE Payment date: 20150128 Year of fee payment: 19 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: S117 Free format text: REQUEST FILED; REQUEST FOR CORRECTION UNDER SECTION 117 FILED ON 18 MAY 2015 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: S117 Free format text: CORRECTIONS ALLOWED; REQUEST FOR CORRECTION UNDER SECTION 117 FILED ON 18 MAY 2015, ALLOWED ON 15 SEPTEMBER 2015 Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20150910 AND 20150916 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 69728076 Country of ref document: DE Representative=s name: MANITZ, FINSTERWALD & PARTNER GBR, DE Ref country code: DE Ref legal event code: R082 Ref document number: 69728076 Country of ref document: DE Representative=s name: LAVOIX MUNICH, DE Ref country code: DE Ref legal event code: R081 Ref document number: 69728076 Country of ref document: DE Owner name: ASCO INDUSTRIES, FR Free format text: FORMER OWNER: ASCOMETAL (S.A.), PUTEAUX, FR |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 20 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R082 Ref document number: 69728076 Country of ref document: DE Representative=s name: MANITZ, FINSTERWALD & PARTNER GBR, DE |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20160127 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20160212 Year of fee payment: 20 Ref country code: ES Payment date: 20160229 Year of fee payment: 20 Ref country code: DK Payment date: 20160129 Year of fee payment: 20 Ref country code: IT Payment date: 20160129 Year of fee payment: 20 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20160131 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: AT Payment date: 20160128 Year of fee payment: 20 Ref country code: FR Payment date: 20160128 Year of fee payment: 20 Ref country code: SE Payment date: 20160128 Year of fee payment: 20 Ref country code: GB Payment date: 20160216 Year of fee payment: 20 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20160108 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20160131 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20160131 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R071 Ref document number: 69728076 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: DK Ref legal event code: EUP Effective date: 20170108 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MK Effective date: 20170107 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: PE20 Expiry date: 20170107 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK07 Ref document number: 262047 Country of ref document: AT Kind code of ref document: T Effective date: 20170108 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: EUG |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FD2A Effective date: 20170426 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 20170107 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 20170109 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: RG Effective date: 20180606 |