EP3274483B1 - Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication - Google Patents

Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication Download PDF

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EP3274483B1
EP3274483B1 EP16718723.6A EP16718723A EP3274483B1 EP 3274483 B1 EP3274483 B1 EP 3274483B1 EP 16718723 A EP16718723 A EP 16718723A EP 3274483 B1 EP3274483 B1 EP 3274483B1
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EP3274483A1 (fr
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Marie-Thérèse PERROT-SIMONETTA
Bernard Resiak
Ulrich Voll
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ArcelorMittal SA
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Definitions

  • the present invention covers the manufacture of parts with high strength properties while being machinable, obtained from steels simultaneously having a good hot ductility for carrying out hot forming operations and hardenability such that it is not possible. no need to perform tempering and tempering operations to get the advertised properties.
  • the invention relates more precisely to parts having, whatever the shape and complexity of the part, a mechanical strength greater than or equal to 1100 MPa, having a yield strength greater than or equal to 700 MPa, an elongation at break A greater than or equal to 12 and a necking with Z-breaking greater than 30%,
  • each part, bar, any form, wire or complex piece obtained by hot forming process is defined as, for example, rolling, or forging with or without subsequent partial or total reheating operations. , thermal or thermochemical treatment and / or shaping with or without removal of material, or even with addition of material as for welding.
  • hot forming of a steel is meant any process that modifies the primary form of a product by an operation which is carried out at a temperature of the material such that the crystalline structure of the steel is predominantly austenitic.
  • micro-alloyed steels ferritic pearlitic structure with different levels of carbon have become widespread in recent decades and are very often used for all kinds of mechanical parts to obtain complex parts without heat treatment directly after hot forming.
  • these steels now have their limits when designers claim mechanical properties exceeding 700 MPa yield strength and 1100 MPa mechanical strength, which often requires them to return to traditional solutions mentioned above.
  • This method involves subjecting the workpiece to a heat treatment having a cooling from a temperature at which the steel is fully austenitic to a temperature Tm of between Ms + 100 D ° C and Ms-20 ° C at a temperature of cooling rate Vr greater than 0.5 ° C / s, followed by holding the workpiece between Tm and Tf, with Tf ⁇ Tm-100 ° C, and preferably Tf ⁇ Tm-60 ° C, for at least 2 minutes to obtain a structure comprising at least 15%, and preferably at least 30% of bainite formed between Tm and Tf.
  • This technique requires many process steps that are detrimental to productivity. We also got to know the patent WO 2009/138586 .
  • the object of the invention is to provide a forging process carried out so as to improve the machinability, by modifying the metallographic structure of the products subjected to the impact load in a fine ferrito-pearlitic structure without adopting the method of tempering and tempering, in order to obtain a limit of elasticity exceeding that obtained by the quenching and tempering process.
  • the tensile strength (Rm) obtained is lower than that obtained by the tempering and tempering process.
  • This method also has the disadvantage of requiring many process steps that complicate the manufacturing process.
  • the absence of precise elements of chemical composition can lead to the use of a chemical composition that is unsuitable for applications of forgings that are detrimental to weldability, machinability or even toughness.
  • the object of the present invention is to solve the problems mentioned above. It aims to provide a steel for hot formed parts with high strength properties, simultaneously having a mechanical strength and a deformation capacity for carrying out hot forming operations.
  • the invention more specifically relates to steels having a mechanical strength greater than or equal to 1100 MPa (ie a hardness greater than or equal to 300 Hv), having a yield strength greater than or equal to 700 MPa, and a higher breaking elongation or equal to 12%, with a failure greater than 30%.
  • the invention also aims to provide a steel with an ability to be produced in a robust manner that is to say without large variations in properties depending on the manufacturing parameters and machinable with commercially available tools without loss of strength. productivity during implementation.
  • the subject of the invention is a part according to claims 1 to 12 and a part manufacturing method according to claim 13.
  • the chemical composition in percentage by weight, must be the following:
  • the carbon content is between 0.10 and 0.30%. If the carbon content is below 0.10% by weight, there is a risk of forming pro-eutectoid ferrite and insufficient mechanical strength. Beyond 0.30%, the weldability becomes more and more reduced because it is possible to form low-tenacity microstructures in the heat-affected zone (ZAT) or in the melted zone. Within this range, the weldability is satisfactory, and the mechanical properties are stable and consistent with the targets of the invention. According to a preferred embodiment, the carbon content is between 0.15 and 0.27% and preferably between 0.17 and 0.25%.
  • the manganese is between 1.6 and 2.1% and preferably between 1.7% and 2.0%. It is a hardening element with solid solution of substitution, it stabilizes the austenite and lowers the transformation temperature Ac3. Manganese therefore contributes to an increase in mechanical strength. A minimum content of 1.6% by weight is necessary to obtain the desired mechanical properties. However, beyond 2.1%, its gammagenic character leads to a significant slowing down of the bainitic transformation kinetics occurring during final cooling and the bainite fraction would be insufficient to achieve a yield strength greater than or equal to 700 MPa. . This combines a satisfactory mechanical strength without increasing the risk of decreasing the bainite fraction and thus reducing the yield strength, nor increasing the quenchability in welded alloys, which would adversely affect the weldability of steel according to the invention.
  • the chromium content should be between 0.5% and 1.7% and preferably between 1.0 and 1.5%.
  • This element makes it possible to control the formation of ferrite on cooling from a completely austenitic structure, because this ferrite, in a large quantity, reduces the mechanical strength required for the steel according to the invention.
  • This element also makes it possible to harden and refine the bainitic microstructure, which is why a minimum content of 0.5% is necessary.
  • this element considerably slows down the kinetics of the bainitic transformation, so, for contents above 1.7%, the bainite fraction may be insufficient to reach a yield strength greater than or equal to 700 MPa.
  • a range of chromium content of between 1.0% and 1.5% is chosen to refine the bainitic microstructure.
  • the silicon must be between 0.5 and 1.0%. In this range, the residual austenite stabilization is made possible by the addition of silicon which considerably slows the precipitation of carbides during bainitic transformation. This has been corroborated by the inventors who have noted that the bainite of the invention is virtually free of carbides. This is because the solubility of silicon in cementite is very low and this element increases carbon activity in austenite. Any formation of cementite will therefore be preceded by a step of rejection of Si at the interface. The enrichment of the austenite carbon, therefore leads to its stabilization at room temperature on the steel according to this first embodiment.
  • the application of an external stress at a temperature below 200 ° C may lead to the transformation of part of this austenite in martensite. This transformation will result in increasing the yield point.
  • the minimum silicon content should be set at 0.5% by weight to achieve the stabilizing effect on the austenite and retard carbide formation.
  • the silicon is less than 0.5%, the elastic limit does not reach the required minimum of 700 MPa.
  • an addition of silicon in an amount greater than 1.0% will induce an excess of residual austenite which will reduce the yield strength.
  • the silicon content will be between 0.75 and 0.9% in order to optimize the aforementioned effects.
  • the niobium should be between 0.065% and 0.15%. It is a micro-alloy element which has the particularity of forming hardening precipitates with carbon and / or nitrogen. It also makes it possible to delay the bainitic transformation, in synergy with the micro-alloy elements such as boron and molybdenum present in the invention.
  • the niobium content must nevertheless be limited to 0.15% to avoid the formation of large precipitates which may be crack initiation sites and to avoid the problems of loss of hot ductility associated with a possible intergranular precipitation of nitrides.
  • the niobium content must be greater than or equal to 0.065% which, combined with titanium, makes it possible to have a stabilizing effect on the final mechanical properties, ie a lower sensitivity to the speed of cooling. Indeed, it can form mixed carbonitrides with titanium and remain stable at relatively high temperatures, which makes it possible to avoid the abnormal magnification of the grains at high temperature, or even allowing sufficiently high refinement of the austenitic grain.
  • the maximum content of Nb is in the range 0.065% and 0.110% to optimize the aforementioned effects.
  • the titanium content should be such that 0.010 ⁇ Ti ⁇ 0.1%.
  • a content maximum of 0.1% is tolerated, above titanium will have the effect of increasing the price and generate harmful precipitates for fatigue resistance and machinability.
  • a minimum of 0.010% is required to control the austenitic grain size and to protect the boron from nitrogen.
  • a range of titanium content of between 0.020% and 0.03% is chosen.
  • the boron content should be between 10 ppm (0.0010%) and 50 ppm (0.0050%).
  • This element makes it possible to control the formation of ferrite on cooling from a completely austenitic structure, because this ferrite, in a large quantity, would reduce the mechanical strength and the elastic limit targeted by the invention. This is a soaking element.
  • a minimum content of 10 ppm is necessary to avoid the formation of ferrite during natural cooling, so generally below 2 ° C / s for the types of parts covered by the invention.
  • above 50 ppm boron will have the effect of forming iron borides that may be harmful to ductility.
  • a range of boron content of between 20 ppm and 30 ppm is chosen to optimize the above-mentioned effects.
  • the nitrogen content should be between 10 ppm (0.0010%) and 130 ppm (0.0130%).
  • a minimum content of 10 ppm is required to form the abovementioned carbonitrides.
  • the nitrogen may cause the bainitic ferrite to become too hard to harden, with possible reduction in the resilience of the finished part.
  • a range of nitrogen content between 50 ppm and 120 ppm is chosen to optimize the aforementioned effects.
  • the aluminum content must be less than or equal to 0.050% and preferably less than or equal to 0.040%, or even less than or equal to 0.020%.
  • the Al content is such that 0.003% ⁇ Al ⁇ 0.015%. This is a residual element whose content we wish to limit.
  • High levels of aluminum are considered to increase erosion of refractories and the risk of clogging of the nozzles during steel casting.
  • aluminum segregates negatively and, it can lead to macro-segregations.
  • aluminum can reduce hot ductility and increase the risk of defects in continuous casting. Without a strong control of the casting conditions, the defects of the micro and macro segregation type ultimately give rise to segregation on the forged part.
  • This band structure consists of alternating bainitic strips with different hardnesses which can adversely affect the formability of the material.
  • the molybdenum content must be less than or equal to 1.0%, preferably less than or equal to 0.5%. Preferably, a molybdenum content range of between 0.03 and 0.15% is chosen. Its presence is favorable for the formation of bainite by synergistic effect with boron and niobium. It thus makes it possible to guarantee the absence of pro-eutectoid ferrite at the grain boundaries. Beyond a content of 1.0%, it promotes the appearance of martensite is not sought.
  • the nickel content must be less than or equal to 1.0%. A maximum level of 1.0% is tolerated, above the nickel will have the effect of increasing the price of the proposed solution, which may reduce its viability from an economic point of view.
  • a range of nickel content between 0 and 0.55% is chosen.
  • the vanadium content must be less than or equal to 0.3%. A maximum content of 0.3% is tolerated, above vanadium will have the effect of increasing the price of the solution and affect the resilience.
  • a vanadium content range of between 0 and 0.2% is selected.
  • Sulfur can be at different levels depending on the desired machinability. There will always be a small quantity because it is a residual element whose value can not be reduced to an absolute zero, but it can also be added voluntarily. A lower S content will be aimed if the desired fatigue properties are very high. In general, we will target between 0.015 and 0.04%, knowing that it is possible to add up to 0.1% to improve machinability. Alternatively, it is also possible to add in combination with sulfur one or more elements selected from tellurium, selenium, lead and bismuth in amounts of less than or equal to 0.1% for each element.
  • the phosphorus must be less than or equal to 0.050% and preferably less than or equal to 0.025%. It is an element that hardens in solid solution but significantly reduces weldability and hot ductility, especially due to its ability to segregate at grain boundaries or its tendency to co-segregate with manganese. For these reasons, its content should be limited to 0.025% in order to obtain good weldability.
  • the copper content must be less than or equal to 0.5%. A maximum content of 0.5% is tolerated because above the copper will have the effect of reducing the fitness of the product.
  • the rest of the composition consists of iron and unavoidable impurities resulting from the elaboration, such as for example arsenic or tin.
  • the criterion S1 is correlated with the robustness of the mechanical properties compared to the variations of cooling conditions in general and in the face of Vr600 variations in particular.
  • the respect of the value ranges of this criterion thus makes it possible to guarantee a very low sensitivity of the grade to the manufacturing conditions.
  • 0.200 ⁇ S1 ⁇ 0.4 0.200 ⁇ S1 ⁇ 0.4, which further improves the robustness.
  • the criteria S2 to S4 are correlated with obtaining a predominantly bainitic structure with more than 70% for the grades according to the invention, thus making it possible to guarantee the attainment of the intended mechanical properties.
  • the heat treatment of income is carried out to ensure the obtaining of very good properties of the parts after cooling.
  • the chemical compositions of the steels used in the tests were collated in Table 1.
  • the reheating temperature of these grades was 1250 ° C.
  • the end temperature of hot shaping was 1220 ° C.
  • the cooling rates Vr600 and Vr400 are shown in Table 2.
  • the parts were cooled between 380 and ambient temperature to 0.15 ° C / s and then machined.
  • the conditions for carrying out the tests and the results of the characterization measurements have been compiled in Table 2.
  • FIG 1 shows the variation of the mechanical strength at break Rm as a function of cooling speed Vr600 for grades A and B.
  • figure 2 shows the variation of the elastic limit Re as a function of the cooling rate Vr600 for the grades A and B.
  • the grade according to the invention has a high stability of its mechanical properties when the cooling conditions vary.
  • the grade is therefore much more robust to variations in process conditions than grades according to the prior art.
  • figure 3 shows the delta of the mechanical strength at break Rm according to criterion S1 for grades A, B and C.
  • figure 4 shows the delta of the elastic limit Re according to criterion S1 for grades A, B and C.
  • the invention will notably be used with advantage for the manufacture of hot formed parts and in particular, hot forged, for applications in land motor vehicles. It also finds applications in the manufacture of parts for boats or in the field of construction, in particular for the manufacture of screw bars for formwork.
  • the invention can be implemented for the manufacture of all types of parts requiring to achieve the properties referred to

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP16718723.6A 2015-03-23 2016-03-23 Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication Active EP3274483B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL16718723T PL3274483T3 (pl) 2015-03-23 2016-03-23 Elementy o strukturze bainitycznej mające właściwości wysokiej wytrzymałości oraz sposób wytwarzania

Applications Claiming Priority (2)

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PCT/IB2015/000384 WO2016151345A1 (fr) 2015-03-23 2015-03-23 Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication
PCT/IB2016/000343 WO2016151390A1 (fr) 2015-03-23 2016-03-23 Pieces a structure bainitique a hautes proprietes de resistance et procede de fabrication

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JP (1) JP6625657B2 (pt)
KR (1) KR101887844B1 (pt)
CN (1) CN107371369B (pt)
AU (1) AU2016238510B2 (pt)
BR (1) BR112017020282B1 (pt)
CA (1) CA2980878C (pt)
EA (1) EA201792077A1 (pt)
ES (1) ES2748436T3 (pt)
HU (1) HUE045789T2 (pt)
MX (1) MX2017012242A (pt)
PL (1) PL3274483T3 (pt)
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WO (2) WO2016151345A1 (pt)

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WO2018215813A1 (en) * 2017-05-22 2018-11-29 Arcelormittal Method for producing a steel part and corresponding steel part
WO2019180492A1 (en) * 2018-03-23 2019-09-26 Arcelormittal Forged part of bainitic steel and a method of manufacturing thereof
FR3123659A1 (fr) 2021-06-02 2022-12-09 Ascometal France Holding Sas Pièce en acier mise en forme à chaud et procédé de fabrication

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JP2888135B2 (ja) * 1994-05-26 1999-05-10 住友金属工業株式会社 高耐久比高強度非調質鋼とその製造方法
FR2744733B1 (fr) 1996-02-08 1998-04-24 Ascometal Sa Acier pour la fabrication de piece forgee et procede de fabrication d'une piece forgee
US6558484B1 (en) * 2001-04-23 2003-05-06 Hiroshi Onoe High strength screw
JP2002115024A (ja) * 2000-10-06 2002-04-19 Nkk Corp 靭性および耐遅れ破壊性に優れた耐摩耗鋼材ならびにその製造方法
JP3888865B2 (ja) 2000-10-25 2007-03-07 株式会社ゴーシュー 鍛造方法
KR100723186B1 (ko) * 2005-12-26 2007-05-29 주식회사 포스코 지연파괴저항성이 우수한 고강도 볼트 및 그 제조기술
FR2931166B1 (fr) * 2008-05-15 2010-12-31 Arcelormittal Gandrange Acier pour forge a chaud a hautes caracteristiques mecaniques des pieces produites
JP5245997B2 (ja) * 2009-04-06 2013-07-24 新日鐵住金株式会社 靭性に優れた高強度熱間鍛造非調質鋼及びその製造方法
JP2011006781A (ja) * 2009-05-25 2011-01-13 Nippon Steel Corp 低サイクル疲労特性に優れた自動車足回り部品とその製造方法
JP5327106B2 (ja) * 2010-03-09 2013-10-30 Ｊｆｅスチール株式会社 プレス部材およびその製造方法
KR101656977B1 (ko) * 2012-04-10 2016-09-12 신닛테츠스미킨 카부시키카이샤 충격 흡수 부재에 적합한 강판과 그 제조 방법
KR20140121229A (ko) * 2013-04-05 2014-10-15 태양금속공업주식회사 인장강도가 우수한 고강도 볼트의 제조방법
DE102013009232A1 (de) * 2013-05-28 2014-12-04 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Bauteils durch Warmumformen eines Vorproduktes aus Stahl

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Publication number Publication date
HUE045789T2 (hu) 2020-01-28
WO2016151345A1 (fr) 2016-09-29
BR112017020282B1 (pt) 2021-08-17
KR101887844B1 (ko) 2018-08-10
ES2748436T3 (es) 2020-03-16
CN107371369A (zh) 2017-11-21
EA201792077A1 (ru) 2018-01-31
BR112017020282A2 (pt) 2018-06-05
EP3274483A1 (fr) 2018-01-31
MX2017012242A (es) 2017-12-15
US20180057909A1 (en) 2018-03-01
AU2016238510B2 (en) 2019-09-19
KR20170118916A (ko) 2017-10-25
JP6625657B2 (ja) 2019-12-25
CA2980878C (fr) 2020-01-14
UA118920C2 (uk) 2019-03-25
JP2018512509A (ja) 2018-05-17
WO2016151390A1 (fr) 2016-09-29
AU2016238510A1 (en) 2017-10-12
PL3274483T3 (pl) 2020-01-31
CN107371369B (zh) 2019-06-21
CA2980878A1 (fr) 2016-09-29

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