EP3168319B1 - Acier haute résistance faiblement allié pour formage à chaud de pièces de haute résistance et de limite élastique élevée - Google Patents

Acier haute résistance faiblement allié pour formage à chaud de pièces de haute résistance et de limite élastique élevée Download PDF

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EP3168319B1
EP3168319B1 EP14897352.2A EP14897352A EP3168319B1 EP 3168319 B1 EP3168319 B1 EP 3168319B1 EP 14897352 A EP14897352 A EP 14897352A EP 3168319 B1 EP3168319 B1 EP 3168319B1
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Prior art keywords
steel
microalloyed
mpa
strength
heat
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German (de)
English (en)
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EP3168319A4 (fr
EP3168319A1 (fr
Inventor
Zuriñe IDOYAGA OLANO
Jacinto José ALBARRÁN SANZ
Oihane CANTERO VIQUIERA
Juan José LARAUDOGOITIA ELORTEGUI
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Sidenor Investigacion y Desarrollo SA
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Sidenor Investigacion y Desarrollo SA
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    • 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
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/064—Dephosphorising; Desulfurising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C2300/00—Process aspects
    • C21C2300/02—Foam creation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C2300/00—Process aspects
    • C21C2300/08—Particular sequence of the process steps

Definitions

  • the present invention relates to a high-strength and high-yield strength microalloyed steel.
  • the invention allows producing a microalloyed steel with high mechanical strength and high yield strength, in addition to responding well to machining operations, based on a given chemical composition, a specific metallurgical process and subsequent controlled cooling.
  • Microalloyed steel is basically classic building steel to which small amounts of alloy elements, such as V, Al, Ti, Nb, Zr, B, etc., capable of forming microprecipitates are added.
  • microalloyed steels The main characteristic of microalloyed steels is based on the occurrence of microprecipitates produced during both the rolling process and the forging process. It is therefore necessary to know the formation and evolution of microprecipitates as a function of thermal cycles, hot deformations and cooling rates in order to dominate the process and produce steel with the desired mechanical properties.
  • microalloyed steels are certain automotive engine components, such as the crankshaft, connecting rods, the rail of common-rail, etc. All these elements are components subjected to high working pressures and stresses, so it is fundamental for them to have very high tensile strength and yield strength values.
  • microalloyed steels of the present patent have a ferrite-perlite structure, and their final application is in heat-forming.
  • microalloyed steel after a heat-forming process is comparable to that of quenched and tempered steel, provided that they both have similar hardness and sulfur content levels.
  • the main advantage derived from the use of microalloyed steels is the direct reduction of the cost of the formed components up to 10-20%, primarily due to the simplification of the manufacturing process by eliminating thermal treatment from quenching and tempering, as well as subsequent straightening operations, stress relief operations, as well as hardening cracks and controls for detecting them.
  • Different microalloyed steel grades are used today according to the strength to be attained in components for which they are going to be used.
  • the characteristics are largely determined by the carbon content of the steel, which can range between 0.15% and 0.50% by weight, as well as the content of other alloying elements, such as Mn and Si, for example, which help with solid solution hardening of ferrite and other microalloying elements such as Ti, V and, in some cases, Nb as well, which form carbide and nitride microprecipitates, functioning as controllers of grain size and precipitation hardening.
  • microalloyed steel grades manufactured today range from 550 MPa to 1000 MPa in terms of strength. These values considerably depend on the thickness of the part and on the forming process and subsequent cooling to which the part is subjected.
  • Patent application no. CN102776439(A)2012 "Niobium microalloying Si-Mn-B series hot forming steel plate and rolling technology” describes a microalloyed steel with Nb but for a flat product with a mechanical strength between 700-900 MPa and a yield strength of 500-600 MPa.
  • Patent application no. CN101629268(A)2010 “Microalloying high-strength and anti-crack flat steel for automobile girder and production process thereof" describes a microalloyed steel in V producing an as-rolled product between 750-850 MPa and a yield strength between 640-700 MPa.
  • Patent application no. CN101307413(A)2008 “Microalloying steel for ultrahigh-strength sucker rod” describes a microalloyed steel with Nb, Ti and V for rods, with a tensile strength greater than 965 MPa.
  • Patent application n° EP2816131 relates to a rolled steel bar for hot forging suitable as a starting material for a common rail used for a diesel engine fuel injection system, a hot forged section material produced by forming the rolled steel bar, the common rail and the method for producing the common rail.
  • the Nb is not present in the rolled steel bar described.
  • Patent application n° EP2159296 refers to a quench hardened and tempered steel and to a method for obtaining parts of said steel.
  • the Nb is not present in the composition of the steel.
  • JPH10121200 discloses a high strength steel material for shear reinforcing bar, excellent in bendability and weldability having a specific composition containing specific amounts of Nb and V and also having a structure composed of ferrite and pearlite.
  • the present invention relates to microalloyed steel for forming high-strength and high-yield strength parts as defined in Claim 1.
  • the steel of the invention consists of a ferrite-perlite structure with mechanical characteristics in which the tensile strength is 1050-1200 MPa, depending on the diameter of the bar and the yield strength is greater than 750 MPa.
  • the invention allows producing a microalloyed steel from a novel chemical composition and a given metallurgical process, having high mechanical strength while at the same time high yield strength, which is fundamental for all automotive components.
  • thermomechanical treatment to which the component formed with the steel in question is subjected has a very important influence on the microstructure, and therefore on the mechanical characteristics of the end component, i.e., the steel with the initial chemical composition must be formed under given conditions and be subjected to controlled cooling under certain conditions in order to achieve the optimized mechanical characteristics of the end component.
  • a synergistic effect has been found between a novel combination of chemical elements and a method of controlled cooling to obtain the characteristics required for said steel.
  • the chemical composition of this steel is designed so that its post-forming process machinability is comparable to or even better than that of classic quenched and tempered steel when they both have similar hardness and sulfur content levels.
  • alloy elements are used in microalloyed steels to improve the tensile strength and other characteristics that allow the use thereof in the discussed applications.
  • Carbon is an essential element for obtaining high strength and hardness, as well as a long fatigue life. In the microalloyed steels, carbon tends to form carbides, hardening and providing strength to said steels.
  • silicon provides solid solution hardening as it dissolves into the ferrite matrix.
  • Manganese prevents the detrimental effect of sulfur, combining with it to form MnS and thereby improving machinability. On the other hand, like silicon, manganese dissolves in the ferrite crystalline network, replacing the iron atoms and causing solid solution hardening.
  • Vanadium is a microalloying element that contributes to refining the grain size and when it combines with carbon, it forms vanadium carbides, which bring about intense precipitation hardening. Vanadium precipitates are hydrogen nucleators, such that in corrosive environments they fix it and improve hydrogen-induced delayed fracture resistance. However, with very high vanadium contents the precipitates coalesce and their effect can become detrimental. Therefore, the optimal vanadium content is between 0.05% and 0.50%.
  • Niobium is a microalloying element having effects similar to those of vanadium on grain size control and on precipitation hardening of the steel, such that it contributes to increasing the mechanical strength and to improving toughness. Furthermore, niobium precipitates fix the hydrogen attacking the steel in corrosive environments, improving the delayed fracture resistance. At more than 0.050%, nevertheless, the precipitates swell, which is detrimental for the mechanical properties, in addition to increasing the risk of the occurrence of bainites. The optimal niobium content is set between 0.001% and 0.050%.
  • the steel proposed by the invention may additionally comprise at least one of the following elements, or a combination thereof, in percentage by weight:
  • Phosphorus hardens the steel and segregates at the austenite grain boundaries, drastically reducing the toughness of the steel. Furthermore, it favors hydrogen embrittlement and delayed fracture. In order to limit its adverse effect, the phosphorus content is limited to less than 0.015%.
  • Chromium is an essential element for assuring steel quenchability; however, since a ferrite-perlite structure is desired for the microalloyed steel of the invention, chromium is an element that must be controlled, hence it is limited to a maximum of 0.50%.
  • Nickel is an element which, at high concentrations, inhibits ferrite formation and furthermore favors quenchability; hence, like chromium, nickel is an element that must be controlled in microalloyed steels. For that reason, it must be limited to a maximum of 0.50%
  • Molybdenum has an effect which greatly favors quenchability, just like chromium and even more than nickel; hence, for a microalloyed steel with a ferrite-perlite structure it is limited to a maximum of 0.10%.
  • the addition of copper prevents steel decarburization and improves corrosion resistance in a manner similar to nickel, inhibiting the growth of corrosion pits.
  • a high copper content impairs hot ductility of the steel such that the upper limit of copper is set at 0.25%.
  • Aluminum is an element that acts like a strong deoxidizer during the steel manufacturing process. Aluminum forms aluminum nitrides which contribute to controlling austenite grain size during heating prior to heat-forming processes. Nevertheless, it forms very hard oxides that are highly detrimental for fatigue life, such that the upper limit thereof is set at less than 0.050%.
  • Nitrogen combines with Ti, Nb, Al and V to form nitrides, the precipitation temperatures of which depend on the respective content of the different elements and on constant features. With a suitable size, those nitrides exert a pinning effect on the austenite grain by controlling its size at a high temperature and preventing coalescence and growth thereof. However, if the nitrogen or microalloying element content is very high, precipitation occurs at a high temperature and the precipitates swell, being rendered ineffective for controlling grain and detrimental for the fatigue life. As a result, the nitrogen content in the steel is limited to 0.004% to 0.020%.
  • This entire method of manufacturing the steel allows achieving the desired sulfur levels and phosphorus levels below 0.015% by weight, in addition to a low inclusion level.
  • the CCT (continuous cooling transformation) diagrams allow knowing the cooling rates suitable for obtaining a ferrite-perlite microstructure in the steel according to the invention.
  • the solidification products are later transformed in heat conditions by means of a process that consists of heating at a temperature between 900-1300°C and a series of consecutive deformations by means of hot forging or rolling until producing an intermediate product having a suitable section, shape and microstructure.
  • the disclosure contemplates the possibility of carrying out a method whereby said steel part can be produced. Said possibility comprises, after producing the steel, the following steps:
  • the method for producing parts made of said steel comprises a heat-forming process, with prior heating at a temperature between 900-1300°C, which allows providing the steel with sufficient hot ductility, in order to give the part of steel a shape similar to that of the end component.
  • the part is subjected to controlled cooling, which will allow achieving the desired mechanical characteristics with a 100% ferrite-perlite structure.
  • said disclosure of the method for manufacturing the microalloyed steel part comprises a machining process machining to obtain the final geometry of the component, hence in order to improve the response of the steel with respect to machinability, the steel can possibly have elements such as sulfur and other elements for improving machinability.
  • a disclosure of the method for producing steel parts comprises the following steps:
  • Table 1 shows the chemical compositions in percentage by weight, the rest being iron and impurities: Table 1 C Mn Si P S Cr Ni Mo V Cu Al Ti N* A 0.36 1.05 0.72 0.009 0.023 0.12 0.09 0.020 0.26 0.13 0.019 0.025 152 B 0.38 1.37 0.72 0.009 0.069 0.15 0.14 0.032 0.25 0.21 0.010 0.009 136 C 0.37 1.39 0.95 0.012 0.073 0.13 0.14 0.034 0.26 0.21 0.008 0.009 207 D 0.40 1.40 1.28 0.010 0.060 0.19 0.13 0.033 0.26 0.20 0.004 0.006 95 E 0.40 1.42 1.51 0.010 0.062 0.18 0.13 0.033 0.25 0.21 0.004 0.006 99 F 0.40 1.16 1.06 0.007 0.063 0.15 0.12 0.028 0.25 0.07 0.009
  • Table 2 shows the values of the mechanical characteristics obtained for one and the same component already formed with all the castings of Table 1.
  • Table 2 Yield strength (MPa) Tensile strength (MPa) Elongation (%) Reduction (%) A 698 954 18 48 B 824 1102 13 25 C 779 1056 9 18 D 880 1140 10 38 E 887 1141 8 32 F 740 1016 18 40 G 648 956 21 41 H 804 1118 15 35
  • steels B-C-D and E have exceeded a strength of 1050 MPa and yield strength of 750 MPa; however, the microstructure of these steels after heat-forming has shown traces of bainites.
  • Figure 1 shows the photographs of the microstructures produced after heat-forming for one and the same part.
  • FIG. 2 shows the details of the bainites found in castings B, C, D and E.
  • steels A and G do not reach a strength of 1000 MPa.
  • Steel A has a low percentage of carbon and manganese, such that it does not reach the strength of 1000 MPa or yield strength of 700 MPa.
  • steel G has a higher percentage of carbon and manganese than steel A does, it has a low percentage of silicon, as well as a low percentage of vanadium, such that precipitation hardening is less than in the case of steel A.
  • Steel F has a tensile strength greater than 1000 MPa and a yield strength of 700 MPa, somewhat greater than steels A and G.
  • the mechanical characteristics object of the present patent have not been achieved due to the percentage of carbon at a level that is somewhat below the suitable level.
  • compositions of steels B and C were designed as a function of the composition of steel A, but increasing the percentages of manganese in the case of steel B and manganese and silicon in the case of steel C. Therefore, even though strengths exceeding 1050 MPa and yield strengths around 800 MPa were achieved, the percentages of bainite obtained were not acceptable for microalloyed steel with a ferrite-perlite microstructure.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (1)

  1. Acier micro-allié de ferrite-perlite de haute résistance à la traction entre 1 050 et 1 200 MPa et de limite élastique élevée supérieure à 750 MPa, comprenant les éléments suivants en pourcentage en poids :
    0,35 % ≤ C ≤ 0,48 %
    0,55 % ≤ Si ≤ 1,40 %
    0,55 % ≤ Mn ≤ 1,40 %
    0,05 % ≤ V ≤ 0,40 %
    0,005 % ≤ Ti ≤ 0,040 %
    0,001 % ≤ Nb ≤ 0,050 %,
    l'acier micro-allié comprenant en outre en option au moins l'un des éléments suivants en pourcentage en poids :
    P ≤ 0,015 %
    S ≤ 0,10%
    Cr ≤ 0,50 %
    Ni ≤ 0,50 %
    Mo ≤ 0,10 %
    Cu ≤ 0,25 %
    0,001 % ≤ Al ≤ 0,050 %
    0,004 % ≤ N ≤ 0,020 %
    Bi ≤ 0,15 %
    Pb ≤ 0,20 %
    Te ≤ 0,02 %
    Se ≤ 0,04 %
    le reste étant formé de fer et d'impuretés.
EP14897352.2A 2014-07-08 2014-07-08 Acier haute résistance faiblement allié pour formage à chaud de pièces de haute résistance et de limite élastique élevée Active EP3168319B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/ES2014/070558 WO2016005615A1 (fr) 2014-07-08 2014-07-08 Acier haute résistance faiblement allié pour formage à chaud de pièces de haute résistance et de limite élastique élevée et procédé pour obtenir des composants de cet acier

Publications (3)

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EP3168319A1 EP3168319A1 (fr) 2017-05-17
EP3168319A4 EP3168319A4 (fr) 2018-01-24
EP3168319B1 true EP3168319B1 (fr) 2020-12-16

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EP (1) EP3168319B1 (fr)
ES (1) ES2860953T3 (fr)
WO (1) WO2016005615A1 (fr)

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KR20200049924A (ko) * 2018-10-29 2020-05-11 현대자동차주식회사 크랭크 샤프트용 강재 및 이를 이용한 크랭크 샤프트 제조방법
JP7189053B2 (ja) * 2019-03-14 2022-12-13 株式会社神戸製鋼所 非調質鍛造用鋼および非調質鍛造部品
CN110643899A (zh) * 2019-10-24 2020-01-03 江阴市恒润重工股份有限公司 一种石化用耐低温锻件的锻造方法
BR112022006127A2 (pt) * 2019-11-18 2022-06-21 Arcelormittal Aço para forjamento de peça mecânica, método de produção de peça mecânica de aço forjada, uso de um aço e veículo
WO2023014332A1 (fr) * 2021-08-04 2023-02-09 Ti̇rsan Kardan Sanayi̇ Ve Ti̇caret Anoni̇m Şi̇rketi̇ Acier micro-allié à haute résistance

Citations (1)

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Publication number Priority date Publication date Assignee Title
JPH10121200A (ja) * 1996-08-26 1998-05-12 Sumitomo Metal Ind Ltd 高強度剪断補強筋用鋼材及びその製造方法

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JP2950702B2 (ja) * 1993-04-01 1999-09-20 新日本製鐵株式会社 高強度熱間鍛造用非調質鋼
FR2833617B1 (fr) * 2001-12-14 2004-08-20 Usinor Procede de fabrication de toles laminees a froid a tres haute resistance d'aciers dual phase micro-allies
EP1408131A1 (fr) * 2002-09-27 2004-04-14 CARL DAN. PEDDINGHAUS GMBH & CO. KG Composition d'un acier et des pièces à partir de cet acier
JP4305216B2 (ja) * 2004-02-24 2009-07-29 Ｊｆｅスチール株式会社 溶接部の靭性に優れる耐サワー高強度電縫鋼管用熱延鋼板およびその製造方法
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EP2159296B1 (fr) * 2007-04-13 2016-03-16 Sidenor Investigacion y Desarrollo, S.A. Acier trempé et durci et procédé permettant de produire des pièces à partir dudit acier
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EP3168319A4 (fr) 2018-01-24
WO2016005615A1 (fr) 2016-01-14
EP3168319A1 (fr) 2017-05-17
ES2860953T3 (es) 2021-10-05

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