EP3469108A1 - Procédé de fabrication d'une bande d'acier laminée à froid présentant des propriétés trip à partir d'un acier à résistance élevée contenant du manganèse - Google Patents

Procédé de fabrication d'une bande d'acier laminée à froid présentant des propriétés trip à partir d'un acier à résistance élevée contenant du manganèse

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Publication number
EP3469108A1
EP3469108A1 EP17730110.8A EP17730110A EP3469108A1 EP 3469108 A1 EP3469108 A1 EP 3469108A1 EP 17730110 A EP17730110 A EP 17730110A EP 3469108 A1 EP3469108 A1 EP 3469108A1
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Prior art keywords
weight
strip
steel
hot
percent
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Granted
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EP17730110.8A
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German (de)
English (en)
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EP3469108B1 (fr
Inventor
Peter PALZER
Thomas Dr. Evertz
Martin Schubert
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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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
    • 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
    • C21D8/0221—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 working steps
    • C21D8/0236—Cold rolling
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • 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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/0221—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 working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/0263—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 following hot rolling
    • 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
    • C21D8/0278—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 involving a particular surface treatment 
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/06—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/02—Superplasticity
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D8/10—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies

Definitions

  • the invention relates to a method for producing a cold-rolled steel strip from a high-strength, manganese-containing steel.
  • Under steel strip are understood in particular steel bands but also steel sheets below. typical
  • Tensile strengths Rm are about 800 MPa to 2000 MPa for these steels.
  • the elongations at break A80 have values of about 3% to 40%.
  • European Patent Application EP 2 383 353 A2 discloses a high-strength manganese-containing steel, a steel strip made from this steel and a method for producing this steel strip.
  • the steel consists of the elements (contents in% by weight and based on the molten steel): C: up to 0.5; Mn: 4 to 12.0; Si: up to 1, 0; AI: up to 3.0; Cr: 0.1 to 4.0; Cu: up to 4.0; Ni: up to 2.0; N: up to 0.05; P: up to 0.05; S: up to 0.01 and balance iron and unavoidable
  • Impurities optionally, one or several elements from the group "V, Nb, Ti" are provided, the sum of the contents of these elements being at most equal to 0.5
  • the steel should be characterized in that it is cheaper to produce than high manganese steels and at the same time high Elongation at break and associated therewith has a significantly improved formability.
  • a method for producing a steel strip from the above-described high-strength manganese-containing steel comprises the following steps:
  • Thin slab is separated as a starting material for the hot rolling or is cast into a cast strip, which is fed as a starting product to the hot rolling,
  • this steel may have a metastable austenite with the capability of stress-induced martensite formation (TRIP effect).
  • Hot-rolled strip has TRIP properties in addition to a high tensile strength.
  • German Offenlegungsschrift DE 197 27 759 A1 discloses a deep-drawable, ultra-high-strength austenitic lightweight structural steel with a tensile strength of up to 1100 MPa, which likewise has TRIP and TWIP properties.
  • the German patent application DE 10 2012 1 1 1 959 A1 describes a high-manganese steel material with TRIP and TWIP properties, which by cold forming below room temperature, preferably in the range of + 25 ° C to -200 ° C, an increase in hardness and formability experiences.
  • TRIP ultra-high-strength austenitic lightweight structural steel with a tensile strength of up to 1100 MPa
  • 2012/0059196 A1 discloses a method for producing hot strip with a horizontal strip casting plant.
  • the hot strip consists of the main components Fe, Mn, Si and Al, has TRIP and / or TWIP properties and is suitable for deep drawing.
  • the patent US 6,358,338 B1 also relates to a method for
  • German published patent application DE 10 2012 013 1 13 A1 describes TRIP steels which have a predominantly ferritic basic structure with retained austenite intercalated. Because of its high work hardening, TRIP steel achieves high levels of uniform elongation and tensile strength.
  • a disadvantage of these manganese-containing steels with TRIP effect is that in the production of a cold-rolled steel strip, the achievable degree of deformation is limited because of the high work hardening of the material during cold rolling and the associated high load on the rolling stands.
  • the present invention based on the object to provide a method for producing a cold rolled steel strip of a high-strength manganese steel with TRIP properties, with which the cold rolling can be designed to a required final thickness more economical and ecological.
  • a production route from the melting of the steel to the cold rolled steel strip to the required final thickness shall be indicated.
  • This object is achieved by a method for producing a steel strip having the features of claim 1.
  • Advantageous embodiments of the invention are specified in the respective subclaims.
  • N max. 0.1, in particular ⁇ 0.05
  • high-strength steels are understood as steels having a tensile strength of 800 MPa to 2000 MPa.
  • the reason for the strong strain hardening of these high-strength manganese-containing steels with a TRIP effect is the proportion of retained austenite present in the microstructure in addition to martensite and / or ferrite and / or bainite and / or perlite.
  • This retained austenite can convert into martensite at appropriate ambient temperatures (TRIP effect, both ⁇ and ⁇ ' -Martensit), wherein at room temperature to about 50 ° C always takes a significant amount of martensite formation by the TRIP effect.
  • TRIP effect ambient temperatures
  • the cold-rolled strip then has a high strength and a low Resumability.
  • TWIP effect Deformation twins
  • cold rolling is commonly associated with cold rolling
  • cold rolling is also used for elevated temperature cold rolling, which is significantly below the AC1 transformation temperature associated with microstructure transformation, unlike hot rolling in cold rolling according to the invention preferably below a homologous temperature, at which just no creeping processes occur in the steel sheet In the single figure 1 shown in the appendix, the influence of the
  • Forming temperature during rolling on the solidification behavior of the material based on the characteristics of tensile tests. Compared to forming at room temperature of 20 ° C, significantly higher elongation values are achieved at forming temperatures of 100 ° C or 200 ° C with a significantly lower increase in tensile strength.
  • a hot strip or a pre-strip to a temperature of above 50 ° C to 400 ° C preferably from 70 ° C to 250 ° C
  • heated or a hot strip or a pre-strip a temperature of above 50 ° C to 400 ° preferably from 70 ° C to 250 ° C
  • already having and then cold rolled to the required final thickness at a temperature before the first pass of above 50 ° C to 400 ° preferably from 70 ° C to 250 ° C.
  • the previous process step may mean reheating, continuous or discontinuous processing utilizing the existing heat in the hot strip or pre-strip, in particular a hot rolling process, or maintaining the temperature in an oven.
  • reheating continuous or discontinuous processing utilizing the existing heat in the hot strip or pre-strip, in particular a hot rolling process, or maintaining the temperature in an oven.
  • a cooling of the strip for example by compressed air or other liquid or gaseous media, take place.
  • the steel strip also has a considerable amount after rolling
  • strain twins results in improved behavior in subsequent reformations against hydrogen induced delayed cracking and hydrogen embrittlement as compared to cold rolling without prior heating with optional annealing process.
  • the steel used for the process according to the invention has a multiphase microstructure consisting of ferrite and / or martensite and / or bainite and / or perlite and retained austenite / austenite.
  • the content of retained austenite / austenite may be 5% to 80%.
  • the retained austenite austenite can partially or completely convert to martensite when mechanical stress is applied due to the TRIP effect.
  • the invention of the underlying alloy has corresponding
  • Dislocation density induced strong solidification (analogous to strain hardening) at room temperature, the steel achieves very high values of elongation at break, in particular of uniform elongation, and tensile strength.
  • this property is achieved by the existing retained austenite only at manganese contents of about 3% by weight.
  • high-strength steel strip which can be provided with a metallic or non-metallic coating, for example based on zinc.
  • a metallic or non-metallic coating for example based on zinc.
  • the steel has a tensile strength Rm of> 800 to 2000 MPa and an elongation at break A80 of 3 to 40%, preferably of> 8 to 40%.
  • the steel has the following alloy composition in% by weight:
  • Al 0.1 to 5, in particular> 0.5 to 3
  • Si 0.05 to 3, in particular> 0.1 to 1.5
  • Nb 0.005 to 0.4, especially 0.01 to 0.1
  • Ta 0.005 to 0.3, especially 0.01 to 0.1
  • Te 0.005 to 0.3, especially 0.01 to 0.1
  • V 0.005 to 0.6, especially 0.01 to 0.3
  • Ca: 0.005 to 0.1 alloying elements are usually added to the steel in order to specifically influence certain properties.
  • An alloying element in different steels can influence different properties. The effect and interaction generally depends strongly on the amount, the presence of other alloying elements and the dissolution state in the material.
  • Connections are versatile and complex.
  • the effect of the alloying elements in the alloy according to the invention will be discussed in more detail.
  • the positive effects of the alloying elements used according to the invention are described below:
  • Carbon C Is required for the formation of carbides, stabilizes the austenite and increases the strength. Higher contents of C deteriorate the welding properties and lead to the deterioration of the elongation and toughness properties, therefore, a maximum content of 0.9% by weight is set.
  • the minimum salary is set at 0.0005% by weight.
  • a content of 0.05 to 0.42% by weight is preferred, since in this range the ratio of retained austenite to other phase fractions can be set particularly advantageously.
  • Manganese Mn Stabilizes austenite, increases strength and toughness, and allows for strain-induced martensite and / or twin formation in the alloy of the present invention. Contents ⁇ 3% by weight are insufficient to stabilize the austenite and thus worsen the elongation properties, while at levels above 12% by weight the austenite is excessively stabilized and thereby the strength properties, in particular the yield strength, are reduced.
  • a range of more than 5 to ⁇ 10% by weight is preferred, since in this range the Ratio of the phase components to each other and the conversion mechanisms during rolling to final thickness can be favorably influenced.
  • Aluminum AI Improves the strength and elongation properties, lowers the specific gravity and influences the conversion behavior of the
  • an Al content of 0.1 to 5% by weight is preferred in order to increase the strength while maintaining good elongation.
  • contents of> 0.5 to 3% by weight allow a particularly high strength and elongation at break.
  • Silicon Si hinders carbon diffusion, reduces specific gravity and increases strength and elongation and toughness properties. Contents of more than 6% by weight prevent further processing by cold rolling due to embrittlement of the material. Therefore, a maximum content of 6% by weight is set. Optionally, a content of 0.05 to 3% by weight is determined, since contents in this range have the forming properties positive
  • Chromium Cr Improves strength and reduces corrosion rate, retards ferrite and pearlite formation and forms carbides.
  • the maximum content is set at 6% by weight because higher contents result in deterioration in elongation properties and significantly higher costs.
  • Manganese steel with average manganese content has a Cr content of 0.1 to 4
  • % By weight preferred to reduce the precipitation of coarse Cr carbides.
  • contents of> 0.5 to 2.5% by weight have proven to be advantageous for the stabilization of austenite and the precipitation of fine Cr carbides.
  • the total content of Al + Si + Cr should be more than 1.2% by weight.
  • Molybdenum Mo acts as a carbide former, increases strength and increases Resistance to delayed cracking and hydrogen embrittlement. Contents of Mo exceeding 3% by weight deteriorate the elongation properties, therefore, a maximum content of 3% by weight is set.
  • a Mo content of 0.005 to 1.5% by weight is preferable in order to avoid the precipitation of large Mo carbides.
  • contents of 0.01 to 0.6% by weight cause the excretion of desired Mo carbides with simultaneously reduced alloying costs.
  • Phosphorus P is a trace element from iron ore and is dissolved in the iron lattice as a substitution atom. Phosphorus increases hardness by solid solution strengthening and improves hardenability. However, it is usually tried to
  • Sulfur S Like phosphorus, it is bound as a trace element in iron ore. It is generally undesirable in steel as it tends to segregate and has a strong embrittlement, resulting in elongation and toughness properties
  • the sulfur content is limited to a maximum of 0.1% by weight.
  • Particularly advantageous is the limitation to ⁇ 0.2% by weight to the
  • Nitrogen N Is also an accompanying element of steelmaking. In the dissolved state, it improves the strength and toughness properties of steels containing more than 4% by weight of manganese-containing Mn. Low Mn-alloyed steels with ⁇ 4% by weight Mn containing free nitrogen tend to be strong
  • the nitrogen diffuses at low temperatures at dislocations and blocks them. He thus causes a strength increase associated with a rapid loss of toughness. Curing of the nitrogen in the form of nitrides is possible, for example, by alloying aluminum, vanadium, niobium or titanium. For the aforementioned reasons, the nitrogen content is limited to a maximum of 0.1% by weight, with contents of ⁇ 0.05% by weight being preferred in order largely to avoid the formation of AIN.
  • Microalloying elements are usually added only in very small amounts ( ⁇ 0.1% by weight per element). They work in contrast to the
  • Typical micro-alloying elements are vanadium, niobium and titanium. These elements can be dissolved in the iron grid and form carbides, nitrides and carbonitrides with carbon and nitrogen.
  • Vanadium V and niobium Nb These have a grain-refining effect, in particular due to the formation of carbides, which at the same time strength, toughness and
  • V 0.6 (V) or 0.4 (Nb)% by weight
  • the contents of V can continue to be 0.01
  • Weight% to 0.3% by weight and the contents of Nb be limited to 0.01 to 0.1% by weight.
  • Tantalum Ta Like niobium, tantalum acts as a carbide-forming agent, enhancing its strength, toughness and elongation properties. Contents of more than 0.5% by weight cause no further improvement in the properties. Therefore, a maximum content of 0.5% by weight is optionally set. Preference is given to a minimum content of 0.005% by weight and a maximum content of 0.3% by weight, in which the grain refining can be advantageously effected. To improve the economy and optimize the grain refining is In particular, a content of from 0.01% by weight to 0.1% by weight is desired.
  • Titanium Ti As a carbide former, it refines grain, improving its strength, toughness, and elongation properties while reducing intergranular corrosion. Contents of Ti more than 1.5% by weight deteriorate the elongation properties, therefore, a maximum content of Ti of 1.5% by weight is determined. Optionally, a minimum content of 0.005 and a maximum content of 0.6% by weight is determined, in which Ti is advantageously eliminated. A minimum content of 0.01% by weight and a maximum content of 0.3 is preferred
  • Weight% provided, which ensures optimum precipitation behavior at low alloying costs.
  • Tin Sn Tin increases the strength but, like copper, accumulates at higher temperatures below the scale and grain boundaries. It leads by penetration into the grain boundaries to the formation of low-melting phases and associated with cracks in the structure and solder brittleness, which is why optionally a maximum content of ⁇ 0.5% by weight is provided. For reasons mentioned above, contents of ⁇ 0.2% by weight are preferably set. In particular, to avoid low-melting phases and cracks in the structure, contents of ⁇ 0.05% by weight are preferred.
  • Copper Cu Reduces the corrosion rate and increases strength. Contents of more than 3% by weight deteriorate the manufacturability by forming low-melting phases during casting and hot rolling, therefore a maximum content of 3
  • Weight% is set.
  • a maximum content of ⁇ 0.5% by weight is provided, in which the occurrence of cracks during casting and hot rolling can be advantageously prevented.
  • Cu contents of ⁇ 0.1% by weight have proven particularly advantageous for avoiding low-melting phases and for preventing cracks.
  • Tungsten W acts as a carbide former and increases strength and heat resistance. Contents of W of more than 5% by weight deteriorate the elongation properties, and therefore a maximum content of 5% by weight is set. Optionally, a maximum content of 3% by weight and a minimum content of 0.01% by weight determined in which advantageously takes place the precipitation of carbides.
  • a minimum content of 0.2% by weight and a maximum content of 1.5% by weight are preferred, which enables optimum precipitation behavior at low alloying costs.
  • Cobalt Co Increases the strength of the steel, stabilizes the austenite and improves the heat resistance. Contents of over 8% by weight worsen the
  • Strength properties favorably influences austenite stability.
  • Zirconium Zr acts as a carbide former and improves strength. Contents of Zr exceeding 0.5% by weight deteriorate the elongation properties, and therefore a maximum content of 0.5% by weight is set.
  • a maximum content of 0.5% by weight is set.
  • a minimum content of 0.01% by weight and a maximum content of 0.2% by weight are provided, which advantageously allow optimal carbide precipitation at low alloying costs.
  • Boron B Delays the austenite transformation, improves the hot working properties of steels and increases the strength at room temperature. It unfolds its effect even at very low alloy contents. Contents above 0.15% by weight greatly deteriorate the elongation and toughness properties, therefore, the maximum content is set to 0.15% by weight.
  • a minimum content of 0.001% by weight and a maximum content of 0.08% by weight is determined, in which the strength-increasing effect of boron is advantageously used.
  • a minimum content of 0.002% by weight and a maximum content of 0.01% by weight which is an optimal use for increasing the strength at
  • Tellurium Te Improves corrosion resistance and mechanical Properties as well as the machinability. Furthermore, Te increases the strength of MnS, which is less elongated in the rolling direction during hot and cold rolling. Contents above 0.5% by weight deteriorate the elongation and toughness properties, and therefore a maximum content of 0.5% by weight is determined. Optionally, a minimum content of 0.005% by weight and a
  • a minimum content of 0.01% by weight and a maximum content of 0.1% by weight are preferred, which allow an optimization of the mechanical properties while reducing the alloying costs.
  • Calcium Ca Used to modify non-metallic oxide inclusions, which could otherwise lead to unwanted alloy failure due to inclusions in the microstructure, which act as stress concentration sites and weaken the metal composite. Furthermore, Ca improves the homogeneity of the alloy according to the invention. In order to develop a corresponding effect, a minimum content of 0.0005% by weight is optionally necessary. Contents above 0.1% by weight bring no further advantage in the inclusion modification, deteriorate the manufacturability and should be avoided due to the high vapor pressure of Ca in molten steel. Therefore, a maximum content of 0.1% by weight is provided.
  • a production route according to the invention from the melting of the steel to the finished steel strip with a required final thickness of less than 10 mm, preferably less than 4 mm, of a high-strength manganese-containing steel comprises the steps:
  • N max. 0.1, in particular ⁇ 0.05
  • Annealing temperature 580 ° C to 820 ° C
  • annealing time 1 minute to 48 hours
  • Annealing temperature 580 ° C to 820 ° C
  • annealing time 1 minute to 48 hours.
  • Typical thickness ranges for pre-strip are 1 mm to 35 mm and for slabs and thin slabs 35 mm to 450 mm.
  • the slab or thin slab is hot rolled to a hot strip having a thickness of 20 mm to 1, 5 mm or hot rolled near the endabunks close cast stock is hot rolled to a hot strip with a thickness of 8 mm to 1 mm.
  • Cold rolled steel strip produced according to the invention has a thickness of
  • Hot rolling is intended for reheating temperatures in the range of 720 ° C to 1200 ° C. If only a few rolling passes are required, the reheat temperature can be selected at the lower end of the range.
  • the hot strip may optionally be subjected to a heat treatment in the temperature range between 580 ° C and 820 ° C for 1 minute to 48 hours, with higher temperatures being associated with shorter treatment times and vice versa.
  • the annealing can be carried out both in a bell annealer (longer annealing times), as well as, for example, in a continuous annealing (shorter annealing times).
  • the optional annealing serves to reduce the strength and / or the increase of the
  • the cold rolling takes place according to the invention increased temperature of the hot strip with the aim to adjust the required thicknesses for the end application of> 0.15 mm to 10 mm of the steel strip.
  • a further annealing process can be carried out optionally coupled with a coating process and finally a skin-pass process with which the surface structure required for the end application is adjusted.
  • the steel strip is hot-dip or electrolytically galvanized or metallic, inorganic or organic coated.
  • a steel strip produced by the process according to the invention has a tensile strength Rm> 800 to 2000 MPa and an elongation at break A80 of 3 to 40%, preferably> 8 to 40%.
  • the cold-rolled steel strip produced according to the invention can then be processed, for example, as a sheet metal section, coil or sheet by cold forming at room temperature or by warm forging at temperatures of 60 ° C to below the AC3, preferably ⁇ 450 ° C to form a component, which due to the considerable Resumability on a Intermediate annealing can be dispensed with depending on the application.
  • the cold-rolled steel strip produced according to the invention can be processed into longitudinally or helically welded tubes, whereby here too, the considerable residual deformability of the steel strip can be dispensed with an intermediate annealing, depending on the application.
  • the tube may have an outer and / or inner metallic, organic or inorganic coating.
  • the tube produced in this way can then be further deformed, for example drawn or expanded, or shaped by means of hydroforming and further processed into a component.
  • Safety steels are used to protect vehicles and buildings against fire and impact, and have high hardness and toughness.
  • the alloys 1 to 4 contain the following elements
  • the steel strips produced from the abovementioned alloys 1 to 4 were cold-rolled for comparison, ie at room temperature and thus below 50 ° C., and also rolled according to the invention at 250 ° C.
  • the measured rolling forces are given below:
  • Cumulative rolling force is understood to mean adding up the rolling forces of the individual passes in order to obtain a comparable measure of the force required.
  • the rolling force was standardized to a bandwidth of 1000 mm.
  • the degree of deformation e is defined as the quotient of the change in thickness Ad of the steel strip examined by the initial thickness dO of the steel strip examined.
  • the rolling force reduction is the calculated reduction in rolling force at 250 ° C as compared with the cold rolling force.
  • the elongation characteristics stand for the elongation in the rolling direction.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un procédé de fabrication d'une bande d'acier laminée à froid à partir d'un acier à résistance élevée contenant du manganèse présentant des propriétés TRIP, contenant (en % en poids) : C: 0,0005 à 0,9 ; Mn : plus de 3,0 jusqu'à 12 ; le reste étant du fer y compris les éléments inévitables accompagnant le fer, avec ajout éventuel d'un ou ou plusieurs des éléments d'alliage suivants (en % en poids) : Al : jusqu'à 10 ; Si : jusqu'à 6 ; Cr : jusqu'à 6 ; Nb : jusqu'à 1,5 ; V : jusqu'à 1,5 ; Ti : jusqu'à 1,5 ; Mo : jusqu'à 3 ; Cu : jusqu'à 3 ; Sn : jusqu'à 0,5 ; W : jusqu'à 5 ; Co : jusqu'à 8 ; Zr : jusqu'à 0,5 ; Ta : jusqu'à 0,5 ; Te : jusqu'à 0,5 ; B : jusqu'à 0,15 ; P : au maximum 0,1, en particulier < 0,04 ; S : au maximum 0,1, en particulier < 0,02 ; N : au maximum 0,1, en particulier < 0,05 ; Ca : jusqu'à 0,1. L'invention vise à améliorer un procédé correspondant. À cet effet, le laminage à froid s'effectue à une épaisseur finale requise à une température avant la première passe supérieure à 50 °C et jusqu'à 400 °C.
EP17730110.8A 2016-06-09 2017-06-08 Procédé de fabrication d'une bande d'acier laminée à froid présentant des propriétés trip à partir d'un acier à résistance élevée contenant du manganèse Active EP3469108B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102016110661.5A DE102016110661A1 (de) 2016-06-09 2016-06-09 Verfahren zur Herstellung eines kaltgewalzten Stahlbandes aus einem hochfesten, manganhaltigen Stahl
PCT/EP2017/063958 WO2017211952A1 (fr) 2016-06-09 2017-06-08 Procédé de fabrication d'une bande d'acier laminée à froid présentant des propriétés trip à partir d'un acier à résistance élevée contenant du manganèse

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EP3469108A1 true EP3469108A1 (fr) 2019-04-17
EP3469108B1 EP3469108B1 (fr) 2024-07-31

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US (1) US20190256943A1 (fr)
EP (1) EP3469108B1 (fr)
KR (1) KR20190020694A (fr)
DE (1) DE102016110661A1 (fr)
RU (1) RU2711696C1 (fr)
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Publication number Priority date Publication date Assignee Title
WO2019209933A1 (fr) * 2018-04-24 2019-10-31 Nucor Corporation Alliages d'acier exempts d'aluminium et leurs procédés de fabrication
CN109440010B (zh) * 2018-12-20 2021-08-13 唐山钢铁集团高强汽车板有限公司 一种1100MPa级高强捆带钢及其生产方法

Family Cites Families (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4533391A (en) * 1983-11-07 1985-08-06 Allegheny Ludlum Steel Corporation Work-hardenable substantially austenitic stainless steel and method
DE19727759C2 (de) * 1997-07-01 2000-05-18 Max Planck Inst Eisenforschung Verwendung eines Leichtbaustahls
FR2796083B1 (fr) * 1999-07-07 2001-08-31 Usinor Procede de fabrication de bandes en alliage fer-carbone-manganese, et bandes ainsi produites
KR101178775B1 (ko) * 2003-12-23 2012-09-07 막스-플랑크-인스티투트 퓌어 아이젠포르슝 게엠베하 경량 구조강의 핫 스트립의 제조 방법
DE102004061284A1 (de) * 2003-12-23 2005-07-28 Salzgitter Flachstahl Gmbh Verfahren zum Erzeugen von Warmbändern aus Leichtbaustahl
DE102005052774A1 (de) * 2004-12-21 2006-06-29 Salzgitter Flachstahl Gmbh Verfahren zum Erzeugen von Warmbändern aus Leichtbaustahl
KR100723164B1 (ko) * 2005-05-03 2007-05-30 주식회사 포스코 가공성이 우수한 냉연강판과 그 제조방법
KR100851158B1 (ko) * 2006-12-27 2008-08-08 주식회사 포스코 충돌특성이 우수한 고망간형 고강도 강판 및 그 제조방법
FR2944789B1 (fr) 2009-04-22 2011-05-20 Rhodia Operations Procede de preparation d'un terpenylcyclohexanol
DE102009030324A1 (de) * 2009-06-24 2011-01-05 Voestalpine Stahl Gmbh Manganstahl und Verfahren zur Herstellung desselben
EP2383353B2 (fr) 2010-04-30 2025-12-31 ThyssenKrupp Steel Europe AG Acier à résistance élevée comprenant du Mn, produit plat en acier composé d'un tel acier et son procédé de fabrication
DE112013001144A5 (de) * 2012-02-25 2014-10-30 Technische Universität Bergakademie Freiberg Verfahren zur Herstellung hochfester Formteile aus hochkohlenstoff- und hochmanganhaltigem austenitischem Stahlguss mit TRIP/TWIP-Eigenschaften
JP5793459B2 (ja) * 2012-03-30 2015-10-14 新日鐵住金ステンレス株式会社 加工性に優れた耐熱フェライト系ステンレス冷延鋼板、冷延素材用フェライト系ステンレス熱延鋼板及びそれらの製造方法
DE102012013113A1 (de) 2012-06-22 2013-12-24 Salzgitter Flachstahl Gmbh Hochfester Mehrphasenstahl und Verfahren zur Herstellung eines Bandes aus diesem Stahl mit einer Mindestzugfestigkleit von 580MPa
CN102912219A (zh) * 2012-10-23 2013-02-06 鞍钢股份有限公司 一种高强塑积trip钢板及其制备方法
DE102012111959A1 (de) * 2012-12-07 2014-06-12 Benteler Automobiltechnik Gmbh Verfahren zur Herstellung eines Kraftfahrzeugbauteils sowie Kraftfahrzeugbauteil
KR101749201B1 (ko) * 2013-05-06 2017-06-20 잘쯔기터 플래시슈탈 게엠베하 경량 강으로 부품을 제조하기 위한 방법
FI126798B (en) * 2013-07-05 2017-05-31 Outokumpu Oy Delayed fracture resistant stainless steel and method for its production
MX387987B (es) * 2013-12-13 2025-03-19 Outokumpu Oy Metodo para producir acero inxoidable duplex de alta resistencia.
WO2015195062A1 (fr) * 2014-06-16 2015-12-23 Hayat Fatih Acier présentant une ductilité supérieure et une haute résistance et son procédé de fabrication
DE102015112886A1 (de) * 2015-08-05 2017-02-09 Salzgitter Flachstahl Gmbh Hochfester aluminiumhaltiger Manganstahl, ein Verfahren zur Herstellung eines Stahlflachprodukts aus diesem Stahl und hiernach hergestelltes Stahlflachprodukt

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Publication number Publication date
RU2711696C1 (ru) 2020-01-21
DE102016110661A1 (de) 2017-12-14
KR20190020694A (ko) 2019-03-04
WO2017211952A1 (fr) 2017-12-14
US20190256943A1 (en) 2019-08-22
EP3469108B1 (fr) 2024-07-31

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