WO2011124851A2 - Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication - Google Patents
Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication Download PDFInfo
- Publication number
- WO2011124851A2 WO2011124851A2 PCT/FR2011/050781 FR2011050781W WO2011124851A2 WO 2011124851 A2 WO2011124851 A2 WO 2011124851A2 FR 2011050781 W FR2011050781 W FR 2011050781W WO 2011124851 A2 WO2011124851 A2 WO 2011124851A2
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- traces
- part according
- steel
- billet
- bar
- Prior art date
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
-
- 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
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Definitions
- the invention relates to steels for mechanical parts with high characteristics, obtained by hot forging or bar machining.
- Certain grades of steel make it possible to obtain high mechanical characteristics on a forged part or a raw rolling bar, without the use of controlled cooling or a subsequent heat treatment. They are based on obtaining a bainitic homogeneous microstructure.
- the object of the invention is to propose mechanical parts made of a given steel grade which, combined with appropriate thermal and thermomechanical treatments, makes it possible simultaneously to obtain mechanical properties (tensile strength Rm, elastic limit Re, ratio Re / Rm, elongation at break A, necking Z) advantageous, and an improved KCU resilience compared to mechanical steel parts known for this same use.
- the subject of the invention is a mechanical part with high characteristics, characterized in that its composition, in percentages by weight, is:
- the remainder being iron and impurities resulting from the preparation, and in that the structure of the steel is bainitic and contains at most 20% in total of martensite and / or pro-eutectoid ferrite and / or perlite.
- the invention also relates to a method of manufacturing a steel part such as a mechanical part with high characteristics, characterized in that it consists of the following steps:
- the billet or hot-formed bar is cooled at a speed giving it a bainitic structure containing at most 20% in total of martensite and / or perlite and / or pro-eutectoid ferrite;
- the billet or hot formed bar can be naturally cooled in still air.
- the billet or hot formed bar can be cooled with air blown.
- the invention is based on a composition of the part and on its combination with a metallurgical structure, barnitic for 80% or more that can be obtained by simple means such as a cooling at the same time. calm or puffed air.
- bainite is meant here as well pure bainite as bainite + residual austenite mixture if the latter is present as is frequently the case, and we include all possible bainite morphologies, including intragranular bainite (also called acicular ferrite). Other phases that may be present, namely martensite, pro-eutectoid ferrite and perlite, must not represent more than 20% of the structure.
- the shades used in the present invention make it possible to obtain, on the basis of a so-called "low-medium” carbon, and by lowering the starting point of transformation mainly by the incorporation of chromium and manganese, tensile strengths. of the order of 1200 MPa or more, for resilience of at least 40 J.cm 2 , up to 70 J.cm 2 .
- the content of C is between 0.05 and 0.25%.
- This interval called “low carbon medium” because its upper limit is in the low zone of the levels considered as carbon means and its lower limit belongs to the field of low carbon, allows a very homogeneous microstructure and hardness even in presence of segregations.
- the hardness of martensitic microstructures that may be present in the segregated zones is only slightly greater than that of the bainitic microstructure.
- these carbon contents allow ductilities and resilience higher than those obtained at the same level of mechanical strength, for contents greater than 0.25%.
- the Mn content is between 1, 2 and 2%.
- Manganese is used, together with chromium, as the main element to lower the formation temperature of bainite (Bs) during continuous cooling. Since a relatively low carbon content is used, relatively high levels of Mn are required, which furthermore must contribute to satisfying the condition imposed on the C, Mn, Cr contents for the calculation of Bs (see below). .
- Manganese is limited to 2% to avoid segregation problems too pronounced.
- the Cr content is between 1, 2 and 2.5%.
- Cr is used in the same way as Mn to lower the bainitic transformation start temperature Bs.
- C, Mn and Cr must be such that 830 - 270 C% - 90 Mn% - 70 Cr% ⁇ 560.
- bainitic transformation start temperature Bs can be classically estimated from the following formula:
- Si can be used to prevent the formation of carbides that would deteriorate resilience during bainitic transformation. At carbon contents below 0.2%, however, this formation of carbides remains weak, and the addition of Si loses its interest from this point of view. On the other hand, by promoting the formation of residual austenite, Si improves fatigue strength for certain applications. In some cases, however, its use can also be excluded by the need to avoid excessive decarburization on the surface.
- Two variants of the invention can therefore be envisaged.
- the Si content results simply from the conditions of preparation, namely the raw materials used and the possible partial oxidation of Si that they brought to the bath of liquid metal, and no significant voluntary addition of Si is performed. In this case, a Si content between traces and 0.3% is typically obtained.
- Si is voluntarily added to obtain a content of 0.8 to 1.5%.
- Ni is between traces and 1%, preferably between traces and 0.5%. It can be present only by its introduction by the raw materials as a residual element, or be added in small quantity to contribute to the decrease of the temperature Bs. But its content is limited to 1%, better 0.5% for reasons of cost, this element being expensive and likely to have its price fluctuate widely on the market.
- Mo is between traces and 0.5%, preferably between 0.04 and 0.5%.
- the role of molybdenum on quenchability is well established: it avoids the formation of ferrite and perlite but does not slow down the formation of bainite. It can therefore be added in variable quantity depending on the diameter of the part.
- a second benefit of molybdenum is to limit susceptibility to reversible brittleness (see Bhadeshia, Mater Sci Forum, High Performance Bainitic Steels, vol 500-501, 2005). Finally, molybdenum strengthens the austenite by passing it in solid solution.
- V is between traces and 0.3%, preferably between 0.05 and 0.3%.
- the addition of vanadium allows additional hardening; however, as compared with ferrito-pearlitic steels, this hardening does not seem to be done by precipitation; it is indeed demonstrated experimentally that after hot deformation (hot forging or rolling) and natural cooling, only a very small fraction of vanadium is in precipitated form.
- vanadium enhances austenite by precipitation and solid solution, and can therefore indirectly contribute to the fineness of the bainitic structure, hence its hardening effect. Its addition is limited to 0.3% for economic reasons.
- Cu is between traces and 1%. It can possibly be used to contribute to hardening, but would lead to implementation difficulties for contents greater than 1%.
- Al is between traces and 0.1%, preferably between 0.005 and 0.1%. Al is optionally added to deoxidize steel and prevent growth excessive austenitic grains during maintenance at high temperature (for example a carburizing treatment) that would be performed on the part after the implementation of the method according to the invention.
- B is between traces and 0.005%, preferably between 0.0005 and 0.005%.
- This optional element can be used for large diameter parts, especially if the Mo content is low, to ensure the homogeneity of the structure (limit the presence of ferrite).
- all the boron will be available to play its role of homogenizer of the structure. It should then have traces ⁇ N ⁇ 0.0080% and Ti% ⁇ 3.5 N%.
- Ti is between traces and 0.03%, preferably between 0.005 and 0.03%. As we have just said, this optional element is to be used mainly for boron shades, with the relationship between Ti% and N% which has just been exposed.
- Nb is between traces and 0.06%. This optional element can be used to refine the austenitic structure after forging or hot rolling, with consequent decrease in bainite package sizes and acceleration of bainite transformation (Bhadeshia, Royal Soc Proc., 2010, Vol 466 p .3).
- S is between traces and 0.1%. As is well known, this element may, if necessary, be left at a relatively high level, or added voluntarily, to improve the machinability of the steel. It is then given a content of 0.005 to 0.1%. Preferably, this significant presence of S is then accompanied by an addition of Ca up to 0.006%, and / or Te up to 0.03%, and / or Se up to 0.05%, and / or or Bi up to 0.05% and / or Pb up to 0.1%.
- This improvement in machinability can be sought in particular for applications where the part is stressed in fatigue, or for applications where its mechanical properties are improved, at least locally, by a sufficient pre-stressing to prevent the propagation of cracks ( crankshaft burnishing, autofrettage of the high-pressure injection rails).
- the other elements contained in the steel according to the invention are iron and impurities resulting from the preparation, present at usual contents.
- the workpiece may be produced by hot forming a billet or bar having the composition described above, such as hot forging or hot rolling, or by machining a bar ready for use. employment.
- the industrial process involves a hot shaping step performed in the austenitic phase (typically 1,100-1250%), followed by natural cooling.
- One of the important points of the invention is the possibility of obtaining high mechanical characteristics without the use of heat treatments after forging or rolling, nor any particular very restrictive control of the rate of cooling which can be carried out naturally, in the air calm. Nevertheless, if the installations allow it, an adaptation of the cooling may in some cases be used, either because of the diameter of the parts (with large parts, too slow cooling can lead to an appearance of ferrite and / or perlite too much), or to obtain mechanical characteristics superior to those which would be obtained by a natural cooling. Air-blast cooling may be sufficient to achieve this objective. Care must be taken, however, that the cooling is not so rapid as to cause a massive appearance of martensite, as a quench would do.
- a low temperature heat treatment (200 to 350 ° C. for periods of 30 minutes to 4 hours) makes it possible to obtain, on the grades according to the invention, a very significant increase in the yield strength. without increasing the hardness and without decreasing the resilience.
- the mechanical characteristics being obtained by natural cooling are also likely to be reached starting from a hot rolled bar ready for use, if it already has the desired metallurgical structure (essentially bainitic) which will be described more far.
- the composition of the steels used in the invention is such that the probability of obtaining the desired structure naturally after a simple air cooling of the hot-rolled bar under usual conditions is not negligible, if the dimensions of the bar lead to an adequate cooling rate.
- results obtained with steel compositions in accordance with the invention and reference compositions are presented. These results are obtained on laboratory castings forged in 40 mm rounds, or on industrial castings forged in circles of equivalent diameter.
- the mechanical characteristics are evaluated after austenitization at ⁇ ⁇ ' ⁇ followed by a natural cooling with calm air or a forced cooling with the blown air.
- two bainitic grades allowing to obtain high mechanical characteristics in the hot forge, and already used on crankshafts, rails and other forgings with high mechanical strength, are added: samples A (corresponding to EP -B-0 787 812) and B (corresponding to EP-A-1 426 453).
- the compositions of these samples are shown in Table 1, along with their bainitic transformation start temperature Bs calculated as previously stated on the basis of C, Mn and Cr contents.
- Ti, Nb and B are typically 0.030%, 0.025% and 0.003% respectively when these elements are present.
- Table 2 presents the mechanical characteristics measured on the products obtained from these samples. It should be emphasized here that the results obtained, in absolute terms, should be analyzed only in the precise context to which they refer. Indeed, it is common to observe differences in the mechanical properties obtained on forgings or rolled parts of the same composition but of different dimensions, generally in the direction of an increase in mechanical characteristics equivalent diameter. The hierarchy between the shades examined will nevertheless remain the same for samples having all the same dimensions, which would be different from those of the examples cited here. The word "AS" after the reference of the sample means that the cooling has, in his case, been led to the supply air. Ech. Structure Re Rm Re / Rm AZ (%) KCU
- the mechanical characteristics of the examples of steels according to the invention C to G thus show a significant increase in the mechanical strength with respect to the medium carbon bainitic grades A and B whose carbon content is in the middle-high carbon category.
- the yield strengths are 60 to 130 MPa higher and the mechanical strengths are 70 to 190 MPa, all things being equal. They also allow an increase of the resilience up to about 100% compared to medium-high carbon grades (C: 50 J / cm 2 against 39 J / cm 2 for A, 32 J / cm 2 for A-As and 27 J / cm 2 for B), always all things being equal.
- the structure is bainitic in all cases, with the exception of E-AS casting cooled with air. This is demonstrated by the ratio Re / Rm which is established at a value of about 0.6, typical of a bainitic structure, except in the case of E-AS where martensite is present and where Re / Rm takes a value. higher.
- a presence of martensite is not in itself prohibitive, insofar as the mechanical characteristics remain very high (in particular the resilience remains greater than 40 J / cm 2 ).
- the fraction of martensite formed is very sensitive to the exact conditions of cooling, one can expect a significant dispersion of the mechanical characteristics on parts made in industrial conditions for which control of room cooling can not always be optimal. It is therefore necessary to set the objective of limiting the total presence of martensite, pro-eutectoid ferrite and perlite to no more than 20%.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2013503161A JP2013533919A (ja) | 2010-04-07 | 2011-04-07 | 鋼製高性能機械部品とその製造方法 |
US13/639,805 US20130037182A1 (en) | 2010-04-07 | 2011-04-07 | Mechanical part made of steel having high properties and process for manufacturing same |
EP11720141A EP2556175A2 (fr) | 2010-04-07 | 2011-04-07 | Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication |
CN201180025478.4A CN102985569B (zh) | 2010-04-07 | 2011-04-07 | 由高特性的钢制成的机械部件及其制备方法 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR1001433A FR2958660B1 (fr) | 2010-04-07 | 2010-04-07 | Acier pour pieces mecaniques a hautes caracteristiques et son procede de fabrication. |
FR1001433 | 2010-04-07 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2011124851A2 true WO2011124851A2 (fr) | 2011-10-13 |
WO2011124851A3 WO2011124851A3 (fr) | 2015-06-25 |
Family
ID=42942210
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/FR2011/050781 WO2011124851A2 (fr) | 2010-04-07 | 2011-04-07 | Pièce mécanique en acier à hautes caractéristiques et son procédé de fabrication |
Country Status (6)
Country | Link |
---|---|
US (1) | US20130037182A1 (fr) |
EP (1) | EP2556175A2 (fr) |
JP (1) | JP2013533919A (fr) |
CN (1) | CN102985569B (fr) |
FR (1) | FR2958660B1 (fr) |
WO (1) | WO2011124851A2 (fr) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2013117953A1 (fr) * | 2012-02-10 | 2013-08-15 | Ascometal | Procédé de fabrication d'une pièce d'acier et pièce d'acier ainsi obtenue |
FR3022259A1 (fr) * | 2014-06-16 | 2015-12-18 | Asco Ind | Acier pour pieces mecaniques a hautes caracteristiques traitees superficiellement, et pieces mecaniques en cet acier et leur procede de fabrication |
US20150376750A1 (en) * | 2013-03-22 | 2015-12-31 | Caterpillar Inc. | Air-hardenable bainitic steel with enhanced material characteristics |
EP3061838A1 (fr) | 2015-02-27 | 2016-08-31 | Swiss Steel AG | Produit longitudinal bainitique nu et son procédé de fabrication |
EP3378957A1 (fr) * | 2017-03-23 | 2018-09-26 | Ascometal France Holding SAS | Acier, procédé pour la fabrication de pièces mécaniques en cet acier, et pièces ainsi fabriquées |
WO2022253912A1 (fr) | 2021-06-02 | 2022-12-08 | Ascometal France Holding Sas | Pièce en acier mise en forme à chaud et procédé de fabrication |
WO2022263887A1 (fr) | 2021-06-16 | 2022-12-22 | Arcelormittal | Procédé de production d'une pièce en acier, et pièce en acier |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN103725980A (zh) * | 2013-10-26 | 2014-04-16 | 溧阳市浙大产学研服务中心有限公司 | 一种高性能磁控连接件 |
JP5876864B2 (ja) * | 2013-12-16 | 2016-03-02 | 株式会社神戸製鋼所 | 舶用鍛鋼品 |
RU2555319C1 (ru) * | 2014-09-15 | 2015-07-10 | Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Южно-Уральский государственный университет" (национальный исследовательский университет) (ФГБОУ ВПО "ЮУрГУ" (НИУ)) | Легкообрабатываемая конструкционная хромомарганцевоникельмолибденовая сталь |
DE102016108633A1 (de) * | 2016-05-10 | 2017-11-30 | Benteler Steel/Tube Gmbh | Kraftstoffeinspritzleitung und rohrförmiger Leitungskanal |
TWI756226B (zh) * | 2016-06-30 | 2022-03-01 | 瑞典商伍德赫爾恩股份有限公司 | 用於工具架之鋼 |
RU2622187C1 (ru) * | 2016-10-31 | 2017-06-13 | Юлия Алексеевна Щепочкина | Конструкционная сталь |
WO2019180492A1 (fr) | 2018-03-23 | 2019-09-26 | Arcelormittal | Pièce forgée en acier bainitique et son procédé de fabrication |
WO2024121606A1 (fr) * | 2022-12-08 | 2024-06-13 | Arcelormittal | Acier forgé et laminé à chaud et son procédé de fabrication |
Citations (2)
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EP0787812B1 (fr) | 1996-02-08 | 2004-03-17 | ASCOMETAL (Société anonyme) | Procédé de fabrication d'une pièce forgée en acier |
EP1426453A1 (fr) | 2002-12-03 | 2004-06-09 | Ascometal | Procédé de fabrication d'une pièce forgée en acier et pièce ainsi obtenue |
Family Cites Families (13)
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JP2768062B2 (ja) * | 1991-06-17 | 1998-06-25 | 株式会社神戸製鋼所 | 高強度強靭鋼の製造方法 |
JPH06212349A (ja) * | 1993-01-14 | 1994-08-02 | Sumitomo Metal Ind Ltd | 高切削性の高靱性非調質高強度鋼とその製造方法 |
JPH06248341A (ja) * | 1993-02-23 | 1994-09-06 | Sumitomo Metal Ind Ltd | 非調質鋼からの高強度高靱性鋼の製造方法 |
JP3524229B2 (ja) * | 1995-08-11 | 2004-05-10 | 株式会社神戸製鋼所 | 高靭性肌焼き鋼製機械部品およびその製法 |
FR2741632B1 (fr) * | 1995-11-27 | 1997-12-26 | Ascometal Sa | Acier pour la fabrication d'une piece forgee ayant une structure bainitique et procede de fabrication d'une piece |
FR2756298B1 (fr) * | 1996-11-26 | 1998-12-24 | Ascometal Sa | Acier et procede pour la fabrication d'une piece de mecanique ayant une structure bainitique |
JP3716073B2 (ja) * | 1997-05-30 | 2005-11-16 | Jfe条鋼株式会社 | 被削性及び疲労特性に優れた熱間鍛造部品の製造方法 |
FR2802607B1 (fr) * | 1999-12-15 | 2002-02-01 | Inst Francais Du Petrole | Conduite flexible comportant des armures en acier bas carbone |
FR2847271B1 (fr) * | 2002-11-19 | 2004-12-24 | Usinor | Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue |
JP3969328B2 (ja) * | 2003-03-26 | 2007-09-05 | 住友金属工業株式会社 | 非調質継目無鋼管 |
JP4269293B2 (ja) * | 2005-10-27 | 2009-05-27 | 日立金属株式会社 | 金型用鋼 |
JP4768447B2 (ja) * | 2006-01-11 | 2011-09-07 | 株式会社神戸製鋼所 | 溶接熱影響部の靭性に優れた耐候性鋼板 |
EP1832667A1 (fr) * | 2006-03-07 | 2007-09-12 | ARCELOR France | Procédé de fabrication de tôles d'acier à très hautes caractéristiques de résistance, de ductilité et de tenacité, et tôles ainsi produites |
-
2010
- 2010-04-07 FR FR1001433A patent/FR2958660B1/fr not_active Expired - Fee Related
-
2011
- 2011-04-07 WO PCT/FR2011/050781 patent/WO2011124851A2/fr active Application Filing
- 2011-04-07 EP EP11720141A patent/EP2556175A2/fr not_active Withdrawn
- 2011-04-07 US US13/639,805 patent/US20130037182A1/en not_active Abandoned
- 2011-04-07 CN CN201180025478.4A patent/CN102985569B/zh not_active Expired - Fee Related
- 2011-04-07 JP JP2013503161A patent/JP2013533919A/ja active Pending
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EP0787812B1 (fr) | 1996-02-08 | 2004-03-17 | ASCOMETAL (Société anonyme) | Procédé de fabrication d'une pièce forgée en acier |
EP1426453A1 (fr) | 2002-12-03 | 2004-06-09 | Ascometal | Procédé de fabrication d'une pièce forgée en acier et pièce ainsi obtenue |
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WO2013117953A1 (fr) * | 2012-02-10 | 2013-08-15 | Ascometal | Procédé de fabrication d'une pièce d'acier et pièce d'acier ainsi obtenue |
US20150376750A1 (en) * | 2013-03-22 | 2015-12-31 | Caterpillar Inc. | Air-hardenable bainitic steel with enhanced material characteristics |
AU2014235986B2 (en) * | 2013-03-22 | 2017-11-16 | Caterpillar Inc. | Air-hardenable bainitic steel with enhanced material characteristics |
FR3022259A1 (fr) * | 2014-06-16 | 2015-12-18 | Asco Ind | Acier pour pieces mecaniques a hautes caracteristiques traitees superficiellement, et pieces mecaniques en cet acier et leur procede de fabrication |
EP2957643A1 (fr) * | 2014-06-16 | 2015-12-23 | ASCO Industries | Acier pour pièces mécaniques à hautes caractéristiques traitées superficiellement, et pièces mécaniques en cet acier et leur procédé de fabrication |
EP3061838A1 (fr) | 2015-02-27 | 2016-08-31 | Swiss Steel AG | Produit longitudinal bainitique nu et son procédé de fabrication |
EP3061837A1 (fr) * | 2015-02-27 | 2016-08-31 | Swiss Steel AG | Produit longitudinal bainitique nu et son procédé de fabrication |
EP3378957A1 (fr) * | 2017-03-23 | 2018-09-26 | Ascometal France Holding SAS | Acier, procédé pour la fabrication de pièces mécaniques en cet acier, et pièces ainsi fabriquées |
FR3064282A1 (fr) * | 2017-03-23 | 2018-09-28 | Asco Industries | Acier, procede pour la fabrication de pieces mecaniques en cet acier, et pieces ainsi fabriquees |
WO2022253912A1 (fr) | 2021-06-02 | 2022-12-08 | Ascometal France Holding Sas | Pièce en acier mise en forme à chaud et procédé de fabrication |
FR3123659A1 (fr) | 2021-06-02 | 2022-12-09 | Ascometal France Holding Sas | Pièce en acier mise en forme à chaud et procédé de fabrication |
WO2022263887A1 (fr) | 2021-06-16 | 2022-12-22 | Arcelormittal | Procédé de production d'une pièce en acier, et pièce en acier |
Also Published As
Publication number | Publication date |
---|---|
WO2011124851A3 (fr) | 2015-06-25 |
EP2556175A2 (fr) | 2013-02-13 |
FR2958660A1 (fr) | 2011-10-14 |
FR2958660B1 (fr) | 2013-07-19 |
CN102985569A (zh) | 2013-03-20 |
CN102985569B (zh) | 2015-08-05 |
US20130037182A1 (en) | 2013-02-14 |
JP2013533919A (ja) | 2013-08-29 |
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