CN110268085A - Automobile high-strength cold-rolled steel sheet - Google Patents

Automobile high-strength cold-rolled steel sheet Download PDF

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Publication number
CN110268085A
CN110268085A CN201780073115.5A CN201780073115A CN110268085A CN 110268085 A CN110268085 A CN 110268085A CN 201780073115 A CN201780073115 A CN 201780073115A CN 110268085 A CN110268085 A CN 110268085A
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impurity
terms
steel plate
rolled steel
cold rolled
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Inventor
T.赫比斯伯格
F.温克尔霍弗
M.施瓦岑布伦纳
E.O.阿曼
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Voestalpine Stahl GmbH
Toyota Motor Corp
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Voestalpine Stahl GmbH
Toyota Motor Corp
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties 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 by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties 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 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/38—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
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/005—Ferrite
    • 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

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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)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The present invention relates to a kind of high strength cold rolled steel plate, have by following element constitute form (in terms of weight %), the tensile strength (R of the poly-phase microcosmos structure including bainite ferrite matrix and 980-1100MPam): C 0.07-0.15, Mn 2.3-3.2, Si 0.6-1.2, Cr 0.05-0.5, Al≤0.2, Nb≤0.1, surplus is Fe in addition to impurity.

Description

Automobile high-strength cold-rolled steel sheet
Technical field
The present invention relates to the high-strength steel sheets (sheet) for being suitable for automobile application.In particular it relates to have At least cold-rolled steel sheet of the tensile strength of 980MPa and excellent formability.
Background technique
For various applications, the strength level of increase is the prerequisite of light construction body, this is in automobile It is particularly true in industry, because the reduction of body quality causes fuel consumption to reduce.
Automobile body parts (part) are usually from steel plate punched, to form complicated thin-slab structure component.However, in this way Part can not be manufactured by conventional high strength steel because formability is too low for complicated structure division.Due to the original The steel (TRIP steel) of cause, multiphase transformation induced plastic auxiliary is constantly subjected to sizable concern in the past few years, in vapour Vehicle main body structure division neutralize as in seat frame material using particularly true.
The poly-phase microcosmos structure that TRIP steel possesses the metastable retained austenite phase including that can generate TRIP effect is (micro- Structure).When making the steel deformation, austenite is changed into martensite, leads to significant processing hardening.The hardening effect plays Resist the effect of the constriction of the material and the delay failure of plate shaping operation.The microstructure of TRIP steel can greatly change it Engineering properties.The most important aspect of the microstructure of TRIP steel is percentage by volume, size and the form of retained austenite phase, because The transformation of austenite to martensite in the steel deformation is directly influenced for these properties.Austenite is set to exist there are several The mode of chemical stabilization at room temperature.In low-alloy TRIP steel, Austria is made by its carbon content and small austenite grain size Family name's body stabilizes.For about 1 weight % of carbon content needed for making stabilization of austenite.However, carbon content high in steel because It damages weldability and can not use in many applications.
Therefore, it is necessary to particularly process approach by carbon enrichment into austenite so that it is stabilized at room temperature.It is common TRIP steel chemical composition also include the other elements added on a small quantity, to help to make stabilization of austenite and auxiliary to form carbon point The microstructure being fitted in austenite.In order to inhibit austenite to decompose during bainite transformation, usually it is always treated as follows Be necessary: silicone content should be about 1.5 weight %.The most common alloying is added to both the Si and Mn of 1.5 weight %.
Steel (TBF)-steel of TRIP- auxiliary with bainite ferrite matrix is to know and attract a large amount of concerns for a long time, It is primarily due to bainite ferrite matrix and realizes excellent stretch flanging (flangability).Moreover, by metastable residual The TRIP effect that austenitic island (island) ensures to the transformation of the strain inducing of martensite, improves their drawability significantly (drawability)。
The formability of TRIP steel is seriously affected by the conversion characteristic of retained austenite phase, the transformation of retained austenite phase Characteristic is then influenced by austenite chemical composition, its form and other factors.In ISIJ International Vol.50 (2010), No.1, p.162-168 in, inquired into the side for influencing that there is at least formability of the TBF steel of the tensile strength of 980MPa Face.However, the cold rolling material investigated in the document is in 950 DEG C of annealing and in the 300-500 DEG C of austempering 200s in salt bath. Therefore, because high annealing temperature, these materials are unsuitable for the production in conventional industrial annealed wire.
However, high Si- content usually used in TBF- steel causes to form silicon oxide layer in steel strip surface, can glue The roller (roller) that is attached in continuous annealing line (CAL) and cause the surface defect on the steel plate then manufactured.Therefore, in recent years To have been devoted to reduce the silicone content in TBF steel.
WO2013/144377 is disclosed with Si and Al alloying and is had the cold rolling TBF- steel of at least 980MPa tensile strength Plate.WO2013/144376 discloses the cold rolling TBF- steel plate that with Si and Cr alloying and tensile strength is at least 980MPa.Although These steel disclose several tempting property, but for having improved property overview in terms of advanced shaping operation (profile) 980MPa steel plate is there are demand, and wherein both local elongation rate and percentage of total elongation are important, such as vapour For structure member in vehicle seats.
Summary of the invention
The present invention relates to high intensity (TBF) steel plates with 980-1100MPa tensile strength and excellent formability, wherein The steel plate can should be manufactured on an industrial scale in continuous annealing line (CAL).The present invention is intended to provide such steel compositions: its Can be processed to especially for automobile seat component, wherein local elongation rate and percentage of total elongation are both important complexity Structure member.However, it is generally accepted that if percentage of total elongation increases, the property such as hole expansibility managed by local elongation rate (HER) or (λ) is deteriorated.
Specific embodiment
The present invention describes in the claims.
The steel plate, which has, forms (%) by what following alloy element was constituted:
Surplus is Fe in addition to impurity.
The limitation of the chemical component of (claimed, the claimed) alloy advocated and the importance of separate element It is hereinafter briefly illustrated with their mutual interactions.Throughout the specification, for all of the chemical composition of steel Percentage is provided with weight % (wt.%).The amount of hard phase is provided with volume % (vol.%).The upper and lower bound of each element It can freely combine in the boundary in the claims.
C:0.07-0.15%
C makes stabilization of austenite and is important for obtaining the enough carbon in retained austenite phase.C is for obtaining the phase The strength level of prestige is also important.Usually it can be expected to every 0.1%C increases the tensile strength of about 100MPa.When C is lower than When 0.07%, then it is difficult to reach the tensile strength of 980MPa.If C is more than 0.15%, weldability is impaired.The upper limit can be 0.14,0.13 or 0.12%.Lower limit can be 0.08,0.09 or 0.10%.Preferred scope is 0.08-0.13%.
Mn:2.3-3.2%
Manganese is that solid solution strengthens (enhancing) element, by reducing MsTemperature and make stabilization of austenite and prevent in cooling Period forms ferrite and pearlite.In addition, Mn makes Ac3Temperature is reduced and is important to stabilization of austenite.It is being less than Under 2.3% content, it may be difficult to obtain the desired retained austenite scale of construction, the tensile strength of 980MPa and austenitizing temperature It may be excessively high for conventional industrial annealed wire.In addition, can be difficult to avoid that polygonal ferrite under lower content It is formed.However, if the amount of Mn be higher than 3.2%, segregation problems can occur because Mn accumulate and result in the liquid phase it is ribbonizing (banding), so that processability be caused potentially to deteriorate.Therefore, the upper limit can be 3.1,3.0,2.9,2.8 or 2.7%.Lower limit can It is 2.3,2.4 or 2.5%.
Si:0.6-1.2%
Si serves as solid solution intensified element and to ensuring that the intensity of sheet metal is important.Si inhibits the precipitating of cementite simultaneously Stabilization of austenite is necessary.
However, if the too high levels, excessive silica will be formed on belt surface, be can lead in CAL Coat the surface defect of (clad) on roller and on the steel plate then manufactured.Therefore, the upper limit be 1.2% and can be limited to 1.1, 1.05,1.0 or 0.95%.Lower limit can be 0.65,0.7,0.75 or 0.80%.Preferred scope is 0.7-1.0%.
Cr:0.05-0.5%
Cr is effective in terms of increasing armor plate strength.Cr is the formation to form ferrite and hinder pearlite and bainite Element.By increasing Cr content, only make Ac3Temperature and MsTemperature slightly reduces.Cr leads to stabilized retained austenite Amount increases.The amount of Cr is restricted to 0.7%.The upper limit can for 0.65,0.60,0.55,0.50,0.45 or 0.40,0.35,0.30 or 0.25%.Lower limit can be 0.10 or 0.15%.Preferred scope is 0.1-0.3%.
Si+Cr:0.9-1.3%
Preferably, the amount of Si+Cr is in the range of 0.9-1.3%, because Si and Cr have collaboration when being added in combination Effect simultaneously causes the amount of retained austenite to increase, and then ductility is caused to be improved.For these reasons, the amount of Si+Cr Preferably it is restricted to 0.9 to 1.2% range.
Al :≤0.2%
Al promotes ferritic formation and also highly useful as deoxidier.MsTemperature increases with Al content and is improved.Al's is another Outer defect is that it leads to Ac3Temperature greatly improves and so that is more difficult to steel the austenitizing in CAL.Due to these originals Cause, Al content are preferably restricted to less than 0.1%, even more preferably less than 0.08%.Therefore Al preferably is used merely for deoxidation. Then, the upper limit can be 0.09,0.08,0.07 or 0.06%.In order to ensure certain effect, lower limit can be set as 0.005,0.01, 0.02 or 0.03%.Nb: < 0.1%
Nb is commonly used in low-alloy steel because of its influence to crystallite dimension to improve intensity and toughness.Nb is due to NbC's Precipitating promotes strength elongation balance by improvement (purification, refine) matrix microstructure and retained austenite phase.Institute Stating steel may include≤0.05%, Nb preferably≤0.03%.According to the present invention, being deliberately added into for Nb is not required.Therefore, The upper limit can be limited to≤0.01%.
Bainite ferrite (TBF) steel plate of high-intensitive TRIP auxiliary of the invention has mainly by embedding in the base Retained austenite field trash constitute microstructure.
Microcosmic composition (constituent) is hereinafter in terms of volume % (vol.%).
The ladle includes bainite ferrite matrix (BF).Therefore, the amount of bainite ferrite is usually >=50% and can For >=55%, >=60% or >=65%.The microstructure also may include tempered martensite (TM).Constituting BF and TM each other can be difficult To distinguish.Therefore, the total content of two kinds of compositions can be restricted to 70-90%.The amount is generally in the range of 80-90%.
Martensite can exist in final microstructure, because depending on its stability, some austenites are in overaging Cooling period at the end of step can be changed into martensite.Martensite can exist with≤15% amount.Untempered martensite Amount is preferably restricted to 10,9,8,7,6 or 5%.These untempered martensite particles are usually close with retained austenite particle It contacts and therefore they is frequently referred to martensite-austenite (MA) particle.
Retained austenite is the prerequisite for obtaining desired TRIP effect.Therefore, the amount of retained austenite should be in 2- 20%, preferably in the range of 5-15%.By the Proc.Int.Conf. in the high-intensitive ferrous alloy assisted about TRIP (2002), Ghent, Belgium, p.61-64 the middle saturated magnetization method being described in detail measures the amount of retained austenite.
Polygonal ferrite (PF) is not that desired microstructure constitutes and is therefore restricted to≤10%, preferably≤5%, ≤ 3% or≤1%.Most preferably, the steel is free of PF.
The engineering properties for the steel advocated is important and should meet at least one claimed below:
Preferably, while meeting all these requirements.
Rm、Rp0.2Value is obtained according to 10002 part 1 of European standard EN, and wherein sample obtains on the longitudinal direction of the band. Percentage of total elongation (A50) obtained according to Japanese Industrial Standards JIS Z 2241:2011, wherein sample obtains in the transverse direction of the band.
The engineering properties of steel plate of the present invention can be greatly adjusted by alloying composition and microstructure.The microstructure It can be adjusted by heat treatment in CAL, particularly by the isothermal treatment temperatures in overage step.
According to an aspect of the present invention, a kind of high strength cold rolled steel plate is provided, is had
A) it is made of (in terms of weight %) what following element was constituted:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising bainite ferrite matrix,
C) tensile strength (R of 980-1100MPam)。
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, claimed below at least one is met ?
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising at least one following (in terms of volume %):
C) at least one of following engineering properties
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, is included
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising (in terms of volume %)
C) at least one of following engineering properties
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, claimed below at least one is met :
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
C) at least one of following engineering properties
Tensile strength (Rm) ≥1020MPa
Yield strength (Rp0.2) ≥800MPa
Yield ratio (Rp0.2/Rm) ≥0.78。
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, is met claimed below: a) by following The composition (in terms of weight %) of composition:
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %):
And/or
C) engineering properties below
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, is met claimed below: a) meet with The composition (in terms of weight %) of lower requirement:
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %)
And/or
C) engineering properties below
According to another aspect of the present invention, a kind of high strength cold rolled steel plate is provided, is met claimed below:
A) meet composition claimed below (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
C) engineering properties below
According to another aspect of the present invention, high strength cold rolled steel plate as defined above is provided, wherein the thickness of the cold-reduced sheet Degree is 1.0-1.6mm, preferably 1.1-1.5mm, more preferably 1.2-1.4mm.
According to another aspect of the present invention, high strength cold rolled steel plate as defined above is provided, wherein bainite ferrite Total content with tempered martensite is 70-90 volume %, preferably 80-90 volume %.
According to another aspect of the present invention, high strength cold rolled steel plate as defined above is provided, wherein tensile strength (Rm) With percentage of total elongation (A50) product be >=13000MPa%, preferably >=13500MPa%.
Embodiment
Table 1 discloses the composition of investigated steel plate.
Embodiment C Si Mn Cr Al
Inventive embodiments 1 0,105 0,81 2,63 0,195 0,045
Inventive embodiments 2 0,106 0,84 2,67 0,197 0,048
Inventive embodiments 3 0,106 0,84 2,67 0,197 0,048
Inventive embodiments 4 0,105 0,81 2,63 0,195 0,045
Inventive embodiments 5 0,118 0,94 2,77 0,17 0,051
The composition for the steel plate that table 1. is investigated
More heat steel alloys are manufactured in conticaster.Slab (slab) is reheated and is hot-rolled down to about 2.8mm to it Thickness.Hot rolling finishing temperature (finishing temperature) is about 900 DEG C and coiling temperature is about 550 DEG C.It will be through heat The time with pickling and the batch annealing 10 hours at about 625 DEG C rolled is to reduce the tensile strength of the band of hot rolling and therefore reduce Cold rolling is exerted oneself.Later, the final thickness that the band is cold-rolled to about 1.4mm in five racks (stand) cold-rolling mill is simultaneously last right It carries out continuous annealing.
Table 2 discloses hot rolling and Cold-rolling Parameters.Implement batch annealing about 10h between hot rolling and cold rolling step.
2. hot rolling of table and Cold-rolling Parameters
Annealing cycle by forming as follows: being heated to about 850 DEG C of temperature, impregnates about 120s, is slow with the rate of about 10 DEG C/s The temperature of slow injection gas cooling to about 750 DEG C is cooled to about 390-400 DEG C out-of-date with the rate fast gas of about 40 DEG C/s Effect temperature, isothermal are maintained at the overaging temperature and are finally cooled to environment temperature.The details handled in CAL is in table 3 It provides.
The parameter handled in table 3.CAL
It was found that material made according to the present invention has excellent engineering properties, as shown in table 4.All embodiments have There is bainite ferrite matrix and includes less than 10% martensite and minimal amount of ferrite.
Particularly, it is also important to note that all inventive embodiments disclose the percentage of total elongation (A greater than 13%50), it is same with this When for all inventive embodiments, the hole expansibility (λ) such as measured by reaming test is more than 52%.
4. engineering properties of table
RmAnd Rp0.Value is obtained according to 10002 part 1 of European standard EN, wherein being tried on the longitudinal direction of the band Sample.Elongation (A50) be according to Japanese Industrial Standards JIS Z 2241:2011 to the sample obtained in the transverse direction of the band and It obtains.
Hole expansibility (λ) is that the average value for three samples for testing (HET) as experience reaming is reported.It passes through basis The reaming test method of ISO/TS16630:2009 (E) and measure.In the test, by the tapered punch with 60 ° of apex angles (punch) compel to enter with 100x 100mm2In the steel plate of size in the punching of manufactured 10mm diameter.One measures first Crackle just stops the test, and measures bore dia in orthogonal both direction.It is calculated using arithmetic mean of instantaneous value.
The following hole expansibility (λ) calculated in terms of %:
λ=(Dh-Do)/Do x 100
The diameter (10mm) and Dh in hole are the diameters of the metapore of the test when wherein Do is beginning.
Industrial applicibility
Material of the invention can be widely applied to the high-strength structure part in automobile.High-strength steel sheet is fitted particularly well There is high requirement and the simultaneously low part of edge crack sensibility for percentage of total elongation for manufacturing.
Claims (according to the 19th article of modification of treaty)
1. high strength cold rolled steel plate has
A) it is made of (in terms of weight %) what following element was constituted:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising the polygonal ferrite of bainite ferrite matrix and≤10 volume %,
C) tensile strength (R of 980-1100MPam)。
2. high strength cold rolled steel plate according to claim 1 meets at least one claimed below
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising at least one following (in terms of volume %):
C) at least one of following engineering properties
3. high strength cold rolled steel plate according to claim 1 or 2, has
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising (in terms of volume %)
C) at least one of following engineering properties
4. meeting at least one claimed below according to the high strength cold rolled steel plate of any one of preceding claims:
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
C) at least one of following engineering properties
Tensile strength (Rm)≥1020MPa
Yield strength (Rp0.2)≥800MPa
Yield ratio (Rp0.2/Rm)≥0.78。
5. high strength cold rolled steel plate according to claim 1 or 2 meets claimed below:
A) by it is following constitute form (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %):
And/or
C) engineering properties below
6. high strength cold rolled steel plate according to claim 3 meets claimed below:
A) meet composition claimed below (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %)
And/or
C) engineering properties below
7. being met claimed below according to the high strength cold rolled steel plate of any one of preceding claims:
A) meet composition claimed below (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
C) engineering properties below
8. according to the high strength cold rolled steel plate of any one of preceding claims, wherein cold-reduced sheet with a thickness of 1.0-1.6mm.
9. according to the high strength cold rolled steel plate of any one of preceding claims, wherein bainite ferrite and tempered martensite is total Content is 70-90 volume %.
10. according to the high strength cold rolled steel plate of any one of preceding claims, wherein tensile strength (Rm) and percentage of total elongation (A50) Product be >=13000MPa%.

Claims (10)

1. high strength cold rolled steel plate has
A) it is made of (in terms of weight %) what following element was constituted:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising bainite ferrite matrix,
C) tensile strength (R of 980-1100MPam)。
2. high strength cold rolled steel plate according to claim 1 meets at least one claimed below
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising at least one following (in terms of volume %):
C) at least one of following engineering properties
3. high strength cold rolled steel plate according to claim 1 or 2, has
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
B) poly-phase microcosmos structure comprising (in terms of volume %)
C) at least one of following engineering properties
4. meeting at least one claimed below according to the high strength cold rolled steel plate of any one of preceding claims:
A) meet the composition (in terms of weight %) of at least one claimed below:
Wherein the impurity meets at least one required as follows:
Surplus is Fe in addition to impurity,
C) at least one of following engineering properties
Tensile strength (Rm)≥1020MPa
Yield strength (Rp0.2)≥800MPa
Yield ratio (Rp0.2/Rm)≥0.78。
5. high strength cold rolled steel plate according to claim 1 or 2 meets claimed below:
A) by it is following constitute form (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %):
And/or
C) engineering properties below
6. high strength cold rolled steel plate according to claim 3 meets claimed below:
A) meet composition claimed below (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
B) poly-phase microcosmos structure comprising (in terms of volume %)
And/or
C) engineering properties below
7. being met claimed below according to the high strength cold rolled steel plate of any one of preceding claims:
A) meet composition claimed below (in terms of weight %):
Wherein the impurity meets following require:
Surplus is Fe in addition to impurity,
And/or
C) engineering properties below
8. according to the high strength cold rolled steel plate of any one of preceding claims, wherein cold-reduced sheet with a thickness of 1.0-1.6mm.
9. according to the high strength cold rolled steel plate of any one of preceding claims, wherein bainite ferrite and tempered martensite is total Content is 70-90 volume %.
10. according to the high strength cold rolled steel plate of any one of preceding claims, wherein tensile strength (Rm) and percentage of total elongation (A50) Product be >=13000MPa%.
CN201780073115.5A 2016-11-25 2017-11-24 Automobile high-strength cold-rolled steel sheet Pending CN110268085A (en)

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PCT/EP2017/080322 WO2018096090A1 (en) 2016-11-25 2017-11-24 High strength cold rolled steel sheet for automotive use

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