EP3222734A1 - Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement - Google Patents

Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement Download PDF

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Publication number
EP3222734A1
EP3222734A1 EP16162073.7A EP16162073A EP3222734A1 EP 3222734 A1 EP3222734 A1 EP 3222734A1 EP 16162073 A EP16162073 A EP 16162073A EP 3222734 A1 EP3222734 A1 EP 3222734A1
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EP
European Patent Office
Prior art keywords
weight
temperature
steel
temperature treatment
manganese
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EP16162073.7A
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German (de)
English (en)
Inventor
Daniel Krizan
Friedrich FÜREDER-KITZMÜLLER
Reinhold Schneider
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Voestalpine Stahl GmbH
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Voestalpine Stahl GmbH
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Priority to EP16162073.7A priority Critical patent/EP3222734A1/fr
Priority to EP17709124.6A priority patent/EP3433386B1/fr
Priority to US16/085,361 priority patent/US20190071748A1/en
Priority to CN201780019271.3A priority patent/CN108884507B/zh
Priority to JP2018549819A priority patent/JP6945545B2/ja
Priority to PCT/EP2017/055714 priority patent/WO2017162450A1/fr
Priority to KR1020187030461A priority patent/KR102246704B1/ko
Priority to ES17709124T priority patent/ES2816065T3/es
Publication of EP3222734A1 publication Critical patent/EP3222734A1/fr
Withdrawn legal-status Critical Current

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    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • C21D1/26—Methods of annealing
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention relates to a method of temperature treating a manganese steel intermediate. It is also a specific alloy of a manganese steel intermediate, which is subjected to a temperature-controlled process in order to obtain a significantly reduced Lüders elongation.
  • Mn manganese
  • medium-manganese steels which are also referred to as medium-manganese steels.
  • the manganese content in weight percent (wt.%) Is often in the range between 3 and 12. Due to its structure, a medium-manganese steel has a high combination of tensile strength and elongation. Typical applications in the automotive industry are complex safety-relevant deep-drawn components.
  • Fig. 1 is a classical, highly schematic diagram shown in which the elongation at break A 80 (in English total elongation called) in percent over the tensile strength (in English tensile strength called) in MPa is plotted.
  • the tensile strength is abbreviated here to R m .
  • the diagram of Fig. 1 gives an overview of the strength classes of currently used steel materials for the automotive industry. In general, the following statement applies: the higher the tensile strength R m of a steel alloy, the lower the elongation at break A 80 of this alloy. In simple terms, it can be stated that the breaking elongation A 80 decreases with increasing tensile strength R m and vice versa. It is therefore necessary to find an optimum compromise between the breaking elongation A 80 and the tensile strength R m for each application.
  • steel alloys In the automotive sector, they work with a whole range of different steel alloys, each of which has been optimized specifically for their particular area of application on the vehicle.
  • alloys For interior and exterior panels, structural parts and bumpers, alloys are used which have good energy absorption.
  • Steel panels for the outer skin of a vehicle are relatively "soft" and have for example a tensile strength R m of about 300 MPa and a good elongation at break A 80 > 30%.
  • the steel alloys of safety-relevant components for example, have a tensile strength R m in the range between 600 and 1000 MPa.
  • the TRIP (transformation-induced plasticity) steels reference numeral 1 in FIG Fig. 1 ).
  • steel alloys which have a high tensile strength R m of usually more than 1000 MPa exhibit.
  • R m tensile strength
  • the new generation of higher-strength AHSS (Advanced High-Strength Steels) steels is suitable (reference 2 in Fig. 1 ).
  • the TBF Trip Bainitic Ferrite
  • the Q & P Quadenching & Partitioning steels.
  • These high-strength AHSS steels have, for example, a manganese content in the range between 1.2 and 3% by weight and a carbon content C which is between 0.05 and 0.25% by weight.
  • the area that is in Fig. 1 designated by the reference numeral 3 comprises medium-manganese steels having an Mn content of between 3 and 12% by weight and a carbon content of ⁇ 1% by weight.
  • An exemplary tensile curve 4 (also called stress-strain curve) is the Fig. 2 refer to.
  • the stress ⁇ in MPa
  • the tensile curve 4 shows an intermediate maximum 5, which is referred to as upper yield strength (R eH ), followed by a plateau 6.
  • upper yield strength R eH
  • plateau 6 changes into a rising curve region.
  • the "length" of the plateau 6 is referred to as Lüders stretch (A L ), as in Fig. 2 shown.
  • a steel product with such a pronounced yield strength can form undesirable luer bands on the surface of components for the automotive industry. Therefore, the pronounced yield strength typically needs to be reduced by a re-rolling process.
  • the aftertreatment in a corresponding Nachwalzwerk (usually with a skin pass mill) is also referred to as tempering.
  • the object to develop a process for the production of manganese steel intermediates in which the Lüdersdehnung is less pronounced.
  • the manganese steel intermediates should have no (measurable) Lüders stretching.
  • the object of the invention is therefore to find an alloy composition and a process for temperature treatment in order to increase the original austenite grain size and to manifest the increased austenite grains in the structure of the medium-manganese steels.
  • the invention aims in a different direction.
  • WO2014095082 A1 a double annealing process that works with different temperatures and processes. Steel products made by the method of WO2014095082 A1 were produced, have a distinct yield strength.
  • the manganese steel intermediates which have been produced from a melt of this manganese steel alloy are subjected to a first temperature treatment process and a subsequent second temperature treatment process within the scope of a temperature treatment according to the invention.
  • the first temperature treatment process is a high temperature process in which the steel intermediate undergoes a first annealing temperature above a critical temperature limit (denoted as T KG ) during a first holding period, this critical temperature limit (T KG ) being defined as follows is: T KG ⁇ (856 - S K * manganese fraction) degrees Celsius, and where S K is a slope value.
  • T KG critical temperature limit
  • the mentioned formula which serves as a definition of the critical temperature limit (T KG ), states that the critical temperature limit (T KG ) in said manganese range decreases with increasing manganese content.
  • the second temperature treatment process is an annealing process in which the steel intermediate is exposed to a second annealing temperature T2, which in any case is lower than the first annealing temperature T1.
  • the first annealing temperature T1 in all embodiments depicts a dependence on said manganese range of the alloy, defined as follows: T1 ⁇ T KG .
  • the first holding period is at least 10 seconds in all embodiments. Particularly preferably, the first holding period in all embodiments is between 10 seconds and 7000 minutes.
  • the second annealing temperature T2 is in all embodiments in the range between the temperatures A 1 and A 3 .
  • the second temperature treatment process including heating the steel intermediate, maintaining the second annealing temperature, and cooling the steel intermediate, takes less than 6000 minutes. Preferably, this total time is even less than 5000 minutes.
  • the invention makes it possible for the first time to provide steel intermediates having a Lüders elongation A L which is less than 3% and preferably less than 1%.
  • the steel intermediates of the invention preferably have in all embodiments a mean primary austenite grain size greater than 3 ⁇ m.
  • the alloy of the steel intermediates of the invention preferably has an average manganese content according to the invention, which means that the manganese content is in the range of 3% by weight ⁇ Mn ⁇ 12% by weight.
  • the manganese content in all embodiments is in the range of 3.5 wt% ⁇ Mn ⁇ 8.5 wt%.
  • the first temperature treatment process is carried out in a continuous strip plant (annealing plant).
  • annealing plant This process is also known as continuous annealing.
  • another possibility is a discontinuous heat treatment (bell annealing) of the steel intermediate.
  • the first temperature treatment of the invention can also be carried out by a special temperature control during hot rolling. At this special Temperature control is taken to ensure that the rolling end temperature of the hot strip during hot rolling in the range above the critical temperature limit T KG .
  • the second temperature treatment process is carried out in a discontinuous plant, the steel intermediate being subjected to the annealing process in this plant in a protective gas atmosphere.
  • This process is preferably carried out in a bell annealing plant.
  • the second temperature treatment process can be carried out in all embodiments but also in a continuous belt plant (annealing) or in a hot-dip galvanizing plant.
  • the steel intermediate of all embodiments may optionally be subjected to a skin pass coating process, which is primarily directed to conditioning the surface of the steel intermediate.
  • a more intensive skin-pass is not required because the steel intermediates of the invention have a low Lüders stretch.
  • the degree of tempering can be reduced or completely avoided.
  • steel intermediates can be made having a Lüders elongation less than 3% and preferably less than 1%.
  • steel intermediates can be produced which have a tensile strength R m (also called minimum strength) which is greater than 490 MPa.
  • the invention can be used to e.g. Cold rolled steel products in the form of cold rolled flat products (e.g., coils).
  • the invention can also be used to e.g. To produce thin sheets or wire and wire products.
  • the invention can also be used to provide hot strip steel products.
  • intermediate steel products is sometimes used when it comes to emphasizing that it is not about the finished steel product but about a preliminary or intermediate product in a multi-stage production process.
  • the starting point for such production processes is usually a melt.
  • the following is an indication of the alloy composition of the melt, since on this side of the manufacturing process it is possible to influence the alloy composition relatively precisely (for example by tartrating constituents, such as alloying elements and optional micro-alloying elements).
  • the alloy composition of the steel intermediate usually deviates only insignificantly from the alloy composition of the melt.
  • Quantities or proportions are here largely in weight percent (short wt.%) Made, unless otherwise stated. If information is provided on the composition of the alloy, or the steel product, then in addition to the explicitly listed materials or materials, the composition comprises iron (Fe) and so-called unavoidable impurities, which always occur in the molten bath and also in the resulting steel intermediate demonstrate. All% by weight must always be supplemented to 100% by weight and all% by volume must always be completed to 100% of the total volume.
  • the temperature treatment of the steel intermediate product comprises a first temperature treatment process S.1 and a subsequent second temperature treatment process S.2. These two temperature treatment processes S.1 and S.2 are in Fig. 3 shown in two temperature-time diagrams shown side by side.
  • the first temperature treatment process S.1 is a high-temperature process in which the steel intermediate is subjected to a first annealing temperature T1 during a first holding period ⁇ 1 (this step is also referred to as holding H1).
  • the annealing temperature T1 is during holding H1 above a critical temperature limit T KG .
  • This critical temperature limit T KG is dependent (inter alia) on the manganese content Mn of the alloy of the manganese steel intermediate, as determined by numerous investigations.
  • Fig. 4 are the critical temperature T K (shown by the straight line 7) and the course of the corresponding critical temperature limit T KG (shown by the straight line 8) shown.
  • the manganese range MnB is plotted in percent by weight.
  • the invention provides excellent results, especially with a manganese content in the following manganese range MnB: 3% by weight ⁇ Mn ⁇ 12% by weight.
  • Fig. 4 For example, the measurement results of four samples are shown using small circle symbols. Further details of these four samples to be understood by way of example and to further samples of the invention are shown in Tables 1 and 2.
  • the alloy composition of the respective type is shown in Table 1, wherein only the essential alloying constituents are mentioned here. For each type, there are a number of embodiments that have been tested. The corresponding examples are numbered in the left column in Table 2 with the numbers 1 to 26.
  • Type 4, 18 represents, for example, the alloy composition of Type 4, Example No. 18.
  • the absolute value 866 in degrees Celsius defines the intersection with the vertical axis and the value S K defines the slope. S K is therefore also called the slope value.
  • the slope value S K is preferably 7.83 ⁇ 10% in all embodiments.
  • the straight line 8 is parallel to the straight line 7.
  • the first annealing temperature T1 must always be above the lower critical temperature limit T KG to ensure that a manganese steel intermediate is obtained in which the Lüders stretching A L is less than 3%.
  • the second temperature treatment process S.2 has an influence on the Lüders strain.
  • the second annealing temperature T2 In order to maintain the grain size of the austenite grains in the microstructure, the second annealing temperature T2 must in any case be lower than the first annealing temperature T1. Since the first annealing temperature T1 is always above the lower critical temperature limit T KG , it can be concluded that the second annealing temperature T2 should preferably be below the lower critical temperature limit T KG .
  • the first annealing temperature T1 is above the temperature limit T KG and that the second annealing temperature T2 is in the range between A 1 and A 3 .
  • the second temperature treatment S.2 is referred to in this case as intercritical annealing.
  • the first holding period ⁇ 1 in all embodiments is preferably at least 10 seconds and preferably between 10 seconds and 6000 minutes.
  • the second holding period ⁇ 2 is at least 10 seconds in all embodiments.
  • the interval between the first temperature treatment process S.1 and the second temperature treatment process S.2 can be selected as needed.
  • the second temperature treatment process S.2 is performed shortly after the first temperature treatment process S.1.
  • Embodiments are preferred in which the first temperature treatment process S.1 including the heating of the steel intermediate product E1, the holding H1 of the first annealing temperature T1 and the cooling Ab1 of the steel intermediate takes less than 7000 minutes.
  • Embodiments are preferred in which the second temperature treatment process S.2 including the heating of the steel intermediate product E2, the holding H2 of the second annealing temperature T2 and the cooling Ab2 of the steel intermediate takes less than 6000 minutes and preferably less than 5000 minutes.
  • the significant reduction of Lüders stretching A L is independent of whether the first temperature treatment process S.1 and / or the second temperature treatment process S.2 in a continuous belt plant (for example in a continuous system) or in a discontinuous plant (for example, in a bell annealer).
  • the invention can be applied to both cold strip intermediates and hot strip intermediates. In both cases a clear reduction of the Lüders strain A L is shown .
  • Fig. 5 shows both the reduction of Lüders elongation A L in percent and the dependence of the mean original Austenitkornificat (D UAK M ) in microns with increasing annealing temperature T1 for two exemplary samples of type 1 and type 2 (see also Table 1), as follows.
  • Fig. 5 For example, in the Type 1 alloy composition tested (represented by curve 9), the critical temperature limit T KG1 is ⁇ 820 ° C if it is desired to achieve a Lüders strain of less than 3% for this Type 1 alloy composition.
  • the curve 10 shows the associated course of the mean original austenite grain boundary D UAK M 1 , as a function of the temperature T1. For the example Type1, a grain size for this results with> 3 ⁇ m.
  • the critical temperature limit T KG2 is ⁇ 970 ° C, if it is desired to achieve a Lüders strain of less than 3% for this type 2 alloy composition.
  • the curve 12 shows the associated course of the mean original austenite grain boundary D UAK M , as a function of the temperature T1.
  • the micro-alloying element niobium (Nb) has a recognizable influence, which is shown as a shift from T KG2 (compared to T KG1 ) to a higher critical temperature for A L ⁇ 3%.
  • Fig. 5 the corresponding lower critical temperature limit T KG1 is shown as a dashed vertical line. It can be seen that the alloy compositions of type 1 from an annealing temperature T1> T KG1 have a mean grain size which is> 3 ⁇ m.
  • the lower critical temperature limit T KG1 is in Fig. 4 characterized by a small black triangle.
  • the microalloying leads to an increase in the critical temperature limit T KG .
  • the critical temperature limit T KG2 is higher by approx. 150 ° C than with the alloy compositions of Type1.
  • the corresponding effective lower critical temperature limit T * KG2 is shown as a dashed vertical line.
  • the resulting average original austenitic grain size in this case is ⁇ 8 ⁇ m.
  • Fig. 6 shows a schematic diagram showing the stress ⁇ in MPa as a function of the strain ⁇ in%.
  • the presentation of the Fig. 6 is with the representation of Fig. 2 to compare, where Fig. 6 only a small section shows.
  • Type 3 alloys of Table 1 were compared here.
  • the type 3 alloys also meet the requirements of the invention. All four samples were each subjected to a first temperature treatment process S.1 and a subsequent second temperature treatment process S.2. All process parameters were identical, except that in the first temperature treatment process S.1, the first annealing temperature T1 was varied as follows (see column 2 of the following Table 3): Table 3 alloy T1 [° C] T2 [° C] Curve typ3 810 640 13.1 typ3 850 640 13.2 typ3 900 640 13.3 typ3 950 640 13.4
  • the solid curve 13.1 of Fig. 6 (Type 3, 14 of Table 2) shows a clearly visible pronounced yield strength and has a Lüders stretching of A L ⁇ 2.60%.
  • the curve 13.2 represents another exemplary sample (Type 3, 15 of Table 2) of the type 3, wherein here yield strength is still slightly pronounced.
  • the curve 13.4 represents a further exemplary sample of the type 3, whereby also here no pronounced yield strength is more visible. This is Type 3, 17 of Table 2.
  • the corresponding measured values (eg for the alloy compositions of Type 1, Type 2 and Type 3) in the range of approximately 700 to 1000 MPa and with an elongation at break A 80 in the range of approximately 20 to 40%.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
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EP16162073.7A 2016-03-23 2016-03-23 Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement Withdrawn EP3222734A1 (fr)

Priority Applications (8)

Application Number Priority Date Filing Date Title
EP16162073.7A EP3222734A1 (fr) 2016-03-23 2016-03-23 Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement
EP17709124.6A EP3433386B1 (fr) 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse.
US16/085,361 US20190071748A1 (en) 2016-03-23 2017-03-10 Method for temperature-treating a manganese steel intermediate product, and steel intermediate product which has been temperature-treated in a corresponding manner
CN201780019271.3A CN108884507B (zh) 2016-03-23 2017-03-10 锰钢中间产品的温度处理方法和以相应方式进行了温度处理的钢中间产品
JP2018549819A JP6945545B2 (ja) 2016-03-23 2017-03-10 マンガン鋼中間材の熱処理方法およびそのような方法によって熱処理される鋼中間材
PCT/EP2017/055714 WO2017162450A1 (fr) 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse et produit intermédiaire en acier-manganèse ayant subi un traitement thermique correspondant
KR1020187030461A KR102246704B1 (ko) 2016-03-23 2017-03-10 상응하는 방식에서 온도-처리된 강 중간 제품 및 망간강 중간 제품의 온도-처리 방법
ES17709124T ES2816065T3 (es) 2016-03-23 2017-03-10 Procedimiento de tratamiento térmico de un producto intermedio de acero al manganeso

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EP16162073.7A EP3222734A1 (fr) 2016-03-23 2016-03-23 Procede de traitement thermique d'un produit intermediaire en acier/manganese et produit intermediaire en acier traite thermiquement

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EP17709124.6A Active EP3433386B1 (fr) 2016-03-23 2017-03-10 Procédé de traitement thermique d'un produit intermédiaire en acier au manganèse.

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US (1) US20190071748A1 (fr)
EP (2) EP3222734A1 (fr)
JP (1) JP6945545B2 (fr)
KR (1) KR102246704B1 (fr)
CN (1) CN108884507B (fr)
ES (1) ES2816065T3 (fr)
WO (1) WO2017162450A1 (fr)

Cited By (2)

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CN108034890A (zh) * 2017-12-13 2018-05-15 天津市宝月钢制品有限公司 低合金中锰耐磨钢热轧板及制备方法
EP3594368A1 (fr) * 2018-07-13 2020-01-15 voestalpine Stahl GmbH Produit intermédiaire d'acier milieu-manganèse-feuillard laminé à froid à teneur en carbone réduite et procédé de fourniture d'un tel produit intermédiaire d'acier

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CN117144261B (zh) * 2023-09-22 2025-09-16 西北工业大学 一种低屈强比高抗拉强度的室温淬火-配分中锰钢及其制备方法

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WO2014095082A1 (fr) 2012-12-21 2014-06-26 Voestalpine Stahl Gmbh Procédé de traitement thermique d'un produit en acier au manganèse et produit en acier au manganèse

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EP3433386B1 (fr) 2020-06-17
EP3433386A1 (fr) 2019-01-30
CN108884507A (zh) 2018-11-23
KR20180127435A (ko) 2018-11-28
JP2019516857A (ja) 2019-06-20
JP6945545B2 (ja) 2021-10-06
CN108884507B (zh) 2020-06-16

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