CN1748039A - Production of cold rolled steel strip with a dual phase ferrite-martensite structure and strips thereby - Google Patents
Production of cold rolled steel strip with a dual phase ferrite-martensite structure and strips thereby Download PDFInfo
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- CN1748039A CN1748039A CNA2004800034661A CN200480003466A CN1748039A CN 1748039 A CN1748039 A CN 1748039A CN A2004800034661 A CNA2004800034661 A CN A2004800034661A CN 200480003466 A CN200480003466 A CN 200480003466A CN 1748039 A CN1748039 A CN 1748039A
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- steel band
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- 229910000734 martensite Inorganic materials 0.000 title claims abstract description 36
- 239000010960 cold rolled steel Substances 0.000 title 1
- 230000009977 dual effect Effects 0.000 title 1
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 58
- 239000010959 steel Substances 0.000 claims abstract description 58
- 238000000034 method Methods 0.000 claims abstract description 27
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 238000005097 cold rolling Methods 0.000 claims abstract description 12
- 238000000137 annealing Methods 0.000 claims abstract description 11
- 238000005098 hot rolling Methods 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 239000000126 substance Substances 0.000 claims abstract description 8
- 238000005496 tempering Methods 0.000 claims abstract description 8
- 238000002791 soaking Methods 0.000 claims description 12
- 229910000859 α-Fe Inorganic materials 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 238000010583 slow cooling Methods 0.000 claims description 7
- 230000006835 compression Effects 0.000 claims description 6
- 238000007906 compression Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 abstract description 12
- 238000004804 winding Methods 0.000 abstract description 3
- 229910000885 Dual-phase steel Inorganic materials 0.000 abstract description 2
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 2
- 238000002360 preparation method Methods 0.000 abstract 1
- 239000011572 manganese Substances 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 239000011651 chromium Substances 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 239000004411 aluminium Substances 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 239000011701 zinc Substances 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 208000034189 Sclerosis Diseases 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007499 fusion processing Methods 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 150000003016 phosphoric acids Chemical class 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
Images
Classifications
-
- 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
-
- 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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D8/0273—Final recrystallisation 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
-
- 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)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
Abstract
The invention relates to a method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure. The inventive method consists in hot rolling a slab having a chemical composition which comprises, by weight, 0.01 % </= C </= 0.1 %, 0.05 % </= Mn </= 1 %, 0.01 % </= Cr </= 1 %, 0.01 % </= Si </= 0.5 %, 0.001 % </= P </= 0.2 %, 0.01 % </= Al </= 0.1 %, N </= 0.01 %, the remainder being iron and impurities resulting from the preparation thereof. The method also comprises the following subsequent steps consisting in: hot winding the band obtained at a temperature of between 550 and 850 DEG C; cold rolling the band with a reduction ratio of between 60 and 90 %; annealing the band continuously in the intercritical region; cooling said band to ambient temperature, in one or more steps, the rate of cooling between 600 DEG C and ambient temperature being between 100 DEG C/s and 1500 DEG C/s; and, optionally, tempering same at a temperature of less than 300 DEG C. The aforementioned annealing and cooling operations are performed such that the end band comprises between 1 and 15 % martensite. The invention also relates to the steel band thus formed.
Description
Technical field
The present invention relates to a kind of method that is used to produce cold rolling ferrite/martensite two-phase steel band, and relate to a kind of steel band that can obtain by this method, more specifically, this steel band is suitable for producing automobile component by deep-draw.
Background technology
Ultrahigh-strength steel is existing development the in recent years, especially in order to satisfy the particular requirement of automotive industry, these require to alleviate the weight of component specifically and therefore reduce the thickness of component, and improve the fatigue strength of component and the security that raising provided of impact property.And these improve the formability necessarily can not weaken the steel plate that is used to produce component.
Therefore, having developed some its structures is the dual phase steel of ferrite/martensite, and this can obtain the tensile strength R greater than 400MPa
m, but do not possess good drawability, because their coefficient of anisotropy is near 1.In addition, their electrodepositable zinc is poor, because they contain a large amount of silicon or other is for fused zinc strip surface being carried out the deleterious composition of good wet.
Steel with phase structure also is known, and these steel have higher average anisotropy coefficient r, but have only medium physical strength, tensile strength R
mBe no more than 400MPa.
As example, can mention that low gap steel and process repeat the Al deoxidization steel of the antirust processing of phosphoric acid salt.The trial of conventional hardening mechanism that improves the steel of these types at all can not improve their mechanical characteristics.In addition, this steel is necessary can be by zinc-plated.
Summary of the invention
The objective of the invention is a kind ofly can carry out deep-draw and have good mechanical property simultaneously and the steel band of good anisotropic properties overcomes the shortcoming of prior art steel by proposing.
For this reason, first purpose of the present invention is a kind of method that is used to produce cold rolling ferrite/martensite two-phase steel band, it is characterized in that, and a kind of slab of hot rolling, the chemical constitution of this slab comprises by weight:
0.010％≤C≤0.100％
0.050％≤Mn≤1.0％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.001％≤P≤0.20％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce,
Described method comprises the following steps:
-be wound on the hot rolled band that obtains under the temperature between 550 ℃ and 850 ℃; Then
-with cold rolling this band of compression ratio between 60% and 90%; Then
-make the continuous annealing in the scope of critical zone of this band; With
-make this band in one or more steps, be cooled to room temperature, the rate of cooling between 600 ℃ and room temperature is between 100 ℃/s and 1500 ℃/s; With
-alternatively, make this band be lower than tempering under 300 ℃ the temperature,
Described annealing and cooling operation be carried out to make described band finally contain 1-15% martensite.
In a preferred implementation method, the chemical constitution of steel also comprises by weight:
0.020％≤C≤0.060％
0.300％≤Mn≤0.500％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.010％≤P≤0.100％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce.
The method according to this invention can also be independently or is comprised following characteristics in combination:
-be higher than the described band of hot rolling under 850 ℃ the temperature;
-described the band of hot rolling under the temperature between 550 ℃ and 750 ℃;
-with the cold rolling described band of compression ratio between 70% and 80%;
The continuous annealing of-described cold-strip comprises the temperature rise period, is soaking (insulation) stage under preset temperature after this temperature rise period;
-soaking temperature is at Ac
1And between 900 ℃;
-soaking temperature is between 750 ℃ and 850 ℃;
-described the room temperature that is cooled to comprises: first slow cooling (slow cooling) step between described soaking temperature and 600 ℃, in this step, rate of cooling is lower than 50 ℃/s, second cooling step of reducing to room temperature for carrying out with the higher rate between 100 ℃/s and the 1500 ℃/s after this first slow cooling step.
Second purpose of the present invention is cold rolling ferrite/martensite two-phase steel band, and its chemical constitution comprises by weight:
In a preferred embodiment, steel band is composed as follows:
0.020％≤C≤0.060％
0.300％≤Mn≤0.500
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.010％≤P≤0.100％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce.
Also comprise following characteristics independently or in combination according to steel of the present invention:
-it has the tensile strength R greater than 450MPa
m
-it has the tensile strength R greater than 500MPa
m
-it has the tensile strength R greater than 600MPa
m
-it has the average anisotropy coefficient r greater than 1.1;
-it has the average anisotropy coefficient r greater than 1.3;
-it also contains the martensite between 1% and 10%;
-it also contains the martensite between 5% and 8%.
At last, the 3rd purpose of the present invention is a kind of according to steel band of the present invention, and this steel band is used for producing automobile component by deep-draw.
The method according to this invention comprises the slab that hot rolling is made of specific composition, and is wound on the hot rolled band that obtains under the temperature between 550 ℃ and 850 ℃ then.
This high temperature operating winding is to developing so-called tissue, and promptly anisotropic structure is favourable.This is because this operating winding can make Fe
3C cementite precipitation is with coalescent and reduce carbon amount in the rework solution during annealing, and this situation is disadvantageous to the development of recrystallized structure.
This method comprises with the compression ratio cold-strip between 60% and 90% and makes the continuous annealing in the scope of critical zone of this band then then.
The most of carbide that forms during the coiling of intercritical annealing permission after recrystallize dissolving mutually.In a single day austenitizing and dissolving that the carbide phase takes place after recrystallize can be retained in the carbon of being caught during the recrystallize and just make this carbon freedom when producing the ferritic structure of recrystallize.Therefore described tissue will not be subjected to the influence of the carbon in the sosoloid as low temperature is reeled, and just suffer damage owing to formed martensitic isotropy feature.
This method comprises then: make this band be cooled to room temperature in one or more steps, the rate of cooling between 600 ℃ and room temperature is between 100 ℃/s and 1500 ℃/s; Make this band be lower than tempering under 300 ℃ the temperature alternatively.
This fast cold step allows to form martensite in the structure of steel, thereby reaches good mechanical property.Yet, must take measures to guarantee can not form too many martensite, because martensite is isotropic, and therefore reduced average anisotropy coefficient r.
Shrend allows to form the carbide phase of suitable vast scale in described composition.Can be by reducing soaking temperature or operating the amount that reduces formed martensitic phase in the scope of critical zone by before quenching, carrying out slow cooling than low value.
Can also reduce nonhomogeneous hardness between ferrite matrix and the martensitic phase by cooling strip material more slowly or by formed martensitic phase after the shrend being continued about 1 minute of short duration tempering operation.
It should be noted that this tempering operation is the overaging operation anything but in prior art as finding.This is especially to have the martensitic effect of inhibition because these overaging of carrying out between 300 ℃ and 500 ℃ are usually handled, and martensite is basal component of the present invention.The tempering of carrying out alternatively according to the present invention comprises makes some be captured in carbon deposition in the sosoloid in the martensite, does not reduce this martensitic ratio simultaneously.The top temperature of this tempering operation is 300 ℃, is preferably 250 ℃, especially is preferably 200 ℃.
Composition according to the present invention comprises the carbon of content between 0.010% and 0.100%.This composition is absolutely necessary for obtaining the favorable mechanical performance, but it necessarily can not have too big amount, because it can cause the excessive martensitic phase of formation ratio.
It also comprises the manganese of content between 0.050% and 1.0%.Manganese improves the yield strength of steel, but greatly reduces its ductility.Why Here it is limits the reason of the content of manganese.
Described composition also comprises the chromium of content between 0.010% and 1.0%, and chromium helps desirable martensite to form.
Described composition also comprises the silicon of content between 0.010% and 0.50%.This has improved the yield strength of steel greatly, but has reduced its ductility slightly, and makes its platability variation.
Described composition also comprises the phosphorus of content between 0.001% and 0.20%, and phosphorus makes the microstructure sclerosis, does not influence its tissue simultaneously.
Described composition also comprises the aluminium of content between 0.010% and 0.10%, and aluminium is caught by nitrogen and prevented to wear out.
Embodiment
Example
As non-limiting example, and, produce the steel of two kinds of grades for the present invention is described better.Their composition thousandth with percentage ratio in following table provides.
| C | Mn | Cr | Si | P | Al | N | |
| A | 60 | 600 | 70 | 70 | 20 | 56 | 5 |
| B | 43 | 373 | 76 | 13 | 22 | 56 | 5.7 |
The rest part of described composition is made of the unavoidable impurities that produces in iron and the fusion process.
Used abbreviation
R
e: yield strength, MPa;
R
m: tensile strength, MPa;
R: coefficient of anisotropy;
P: flation (plateau);
%m: ratio of martensite
After producing, the austenitizing that the steel of two kinds of grades was carried out under 1250 ℃ 1 hour is so that the dissolved aluminum nitride.Hot rolling slab then is so that the temperature when making rolling the end is higher than 900 ℃, the AR of the steel of two kinds of grades
3Value all is about 870 ℃.
Cool off this hot rolled band with the rate of cooling of about 25 ℃/s by shrend then, up to reaching the coiling temperature.At 720 ℃ of following coiling A level steel, and at a sample of 550 ℃ of following coiling B level steel, at 720 ℃ of another samples of reeling down.
Cold rolling then each sample so that reach 75% compression ratio, carries out anneal for some samples subsequently, and carries out anneal for other sample under 800 ℃ soaking temperature under 750 ℃ soaking temperature.Reduce to the cooling of room temperature then by shrend with the speed of about 25 ℃/s.
Then, measure the mechanical property and the anisotropic properties of resulting steel.
Outcome record is in following table.
| Grade | T Reel (℃) | T Soaking (℃) | Direction | R e (MPa) | R m (MPa) | P (％) | r | Mean value r | ％m |
| A | 720 | 800 | T | 420 | 711 | 0 | 1.10 | 0.98 | 14 |
| L | 405 | 713 | 0 | 1.11 | |||||
| 45° | 425 | 720 | 0 | 0.85 | |||||
| 750 | T | 443 | 713 | 0 | 1.26 | 1.02 | 12 | ||
| L | 438 | 717 | 0 | 1.13 | |||||
| 45° | 451 | 736 | 0 | 0.84 |
| B | 720 | 800 | T | 432 | 656 | 0 | 1.46 | 1.27 | 8 |
| L | 430 | 697 | 0 | 1.60 | |||||
| 45° | 436 | 668 | 0 | 1.01 | |||||
| 750 | T | 454 | 662 | 0 | 2.04 | 1.37 | 7 | ||
| L | 457 | 690 | 0 | 1.41 | |||||
| 45° | 461 | 677 | 0 | 1.01 | |||||
| 550 | 800 | T | 455 | 677 | 0 | 1.47 | 1.21 | 6 | |
| L | 446 | 667 | 0 | 1.44 | |||||
| 45° | 472 | 687 | 0 | 0.97 | |||||
| 750 | T | 475 | 680 | 0.3 | 1.46 | 1.09 | 5 | ||
| L | 463 | 668 | 0.4 | 1.25 | |||||
| 45° | 482 | 697 | 0.3 | 0.83 |
Determine the overall anisotropy of steel by average normal coefficient of anisotropy r:
Wherein, r
TRepresentative is along the r value that laterally records of strip-rolling direction, r
LThe r value that representative is vertical along band or rolling direction records, and r
45 °Representative with strip-rolling direction direction at 45 on the r value that records.
For 720 ℃ rolling temperature, Fig. 1 illustrates the mean coefficient r of A level steel and B level steel and the relation between the formed martensite content %m.As can be seen, martensite content is high more, and the anisotropy of steel is obvious more.
It can also be seen that martensite content is high more, mechanical property is high more.
As an illustration, Fig. 2 illustrates the microstructure of utilizing A level steel to obtain, at 720 ℃ of these A level steel of reeling down, anneals under 750 ℃ then, so that obtain 12% martensite at last.Can clearly distinguish formed ferrite and martensite in the drawings.
Claims (22)
1. a method that is used to produce cold rolling ferrite/martensite two-phase steel band is characterized in that, a kind of slab of hot rolling, and the chemical constitution of this slab comprises by weight:
0.010％≤C≤0.100％
0.050％≤Mn≤1.0％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.001％≤P≤0.20％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce, and described method also comprises the following steps:
-be wound on the hot rolled band that obtains under the temperature between 550 ℃ and 850 ℃; Then
-with cold rolling this band of compression ratio between 60% and 90%; Then
-make the continuous annealing in the scope of critical zone of this band; With
-make this band in one or more steps, be cooled to room temperature, the rate of cooling between 600 ℃ and room temperature is between 100 ℃/s and 1500 ℃/s; With
-alternatively, make this band be lower than tempering under 300 ℃ the temperature,
Described annealing and cooling operation be carried out to make described band finally contain 1-15% martensite.
2. the method for claim 1 is characterized in that, the chemical constitution of described steel comprises:
0.020％≤C≤0.060％
0.300％≤Mn≤0.500％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.010％≤P≤0.100％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce.
3. a method as claimed in claim 1 or 2 is characterized in that, is being higher than the described band of hot rolling under 850 ℃ the temperature.
4. one kind as each described method among the claim 1-3, it is characterized in that the described band of hot rolling under the temperature between 550 ℃ and 750 ℃.
5. one kind as each described method among the claim 1-4, it is characterized in that, with the cold rolling described band of compression ratio between 70% and 80%.
6. one kind as each described method among the claim 1-5, it is characterized in that the continuous annealing of described cold-strip comprises the temperature rise period, is the soaking stage under preset temperature after this temperature rise period.
7. a method as claimed in claim 6 is characterized in that soaking temperature is at Ac
1And between 900 ℃.
8. a method as claimed in claim 7 is characterized in that, soaking temperature is between 750 ℃ and 850 ℃.
9. one kind as each described method among the claim 1-8, it is characterized in that, the described room temperature that is cooled to comprises: the first slow cooling step between described soaking temperature and 600 ℃, in this first slow cooling step, rate of cooling is lower than 50 ℃/s, second cooling step of reducing to room temperature for carrying out with the higher rate between 100 ℃/s and the 1500 ℃/s after this first slow cooling step.
10. a method as claimed in claim 9 is characterized in that, carries out described second cooling step by shrend.
11. one kind as each described method among the claim 1-8, it is characterized in that, carries out described cooling with the rate of cooling between 100 ℃/s and the 1500 ℃/s in a single operation.
12. a method as claimed in claim 11 is characterized in that, carries out described cooling by shrend.
13. a cold rolling ferrite/martensite two-phase steel band, the chemical constitution of this steel band comprises by weight:
0.010％≤C≤0.100％
0.050％≤Mn≤1.0％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.001％≤P≤0.20％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce, and this steel band also contains the martensite between 1% and 15%.
14. a steel band as claimed in claim 13 is characterized in that, the chemical constitution of this steel band also comprises:
0.020％≤C≤0.060％
0.300％≤Mn≤0.500％
0.010％≤Cr≤1.0％
0.010％≤Si≤0.50％
0.010％≤P≤0.100％
0.010％≤Al≤0.10％
N≤0.010％
Rest part is the impurity that iron and melting produce.
15. one kind as claim 13 or 14 described steel bands, it is characterized in that this steel band has the tensile strength R greater than 450MPa
m
16. a steel band as claimed in claim 15 is characterized in that this steel band has the tensile strength R greater than 500MPa
m
17. a steel band as claimed in claim 16, its feature are that also this steel band has the tensile strength R greater than 600MPa
m
18. one kind as each described steel band among the claim 13-17, it is characterized in that this steel band has the average anisotropy coefficient r greater than 1.1.
19. a steel band as claimed in claim 18 is characterized in that, this steel band has the average anisotropy coefficient r greater than 1.3.
20. one kind as each described steel band among the claim 13-19, it is characterized in that this steel band also contains the martensite between 1% and 10%.
21. a steel band as claimed in claim 20 is characterized in that this steel band also contains the martensite between 5% and 8%.
22. application that is used for producing automobile component as each described steel band among the claim 13-21 by deep-draw.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FR0301358A FR2850671B1 (en) | 2003-02-05 | 2003-02-05 | PROCESS FOR MANUFACTURING A DUAL-PHASE STEEL BAND HAVING A COLD-ROLLED FERRITO-MARTENSITIC STRUCTURE AND A BAND OBTAINED THEREFROM |
| FR03/01358 | 2003-02-05 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1748039A true CN1748039A (en) | 2006-03-15 |
| CN100465299C CN100465299C (en) | 2009-03-04 |
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ID=32696392
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004800034661A Expired - Lifetime CN100465299C (en) | 2003-02-05 | 2004-01-30 | Production of cold rolled steel strip with a dual phase ferrite-martensite structure and strips thereby |
Country Status (16)
| Country | Link |
|---|---|
| US (1) | US20060144482A1 (en) |
| EP (1) | EP1592816B1 (en) |
| JP (1) | JP4528769B2 (en) |
| KR (1) | KR101091021B1 (en) |
| CN (1) | CN100465299C (en) |
| BR (1) | BRPI0407236A (en) |
| CA (1) | CA2514736C (en) |
| ES (1) | ES2831249T3 (en) |
| FR (1) | FR2850671B1 (en) |
| HU (1) | HUE052206T2 (en) |
| MX (1) | MXPA05008189A (en) |
| PL (1) | PL206109B1 (en) |
| RU (1) | RU2341566C2 (en) |
| UA (1) | UA87454C2 (en) |
| WO (1) | WO2004079022A1 (en) |
| ZA (1) | ZA200505968B (en) |
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| CN102115808A (en) * | 2010-11-17 | 2011-07-06 | 莱芜钢铁股份有限公司 | Ferrite region rolling temperature control system |
| CN103952523A (en) * | 2014-04-15 | 2014-07-30 | 东北大学 | Continuous annealing method of martensitic ferritic dual-phase steel cold-rolled strip |
| CN105401071A (en) * | 2015-12-22 | 2016-03-16 | 武汉钢铁(集团)公司 | Galvanized dual-phase steel for 500 MPa class car and production method |
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-
2003
- 2003-02-05 FR FR0301358A patent/FR2850671B1/en not_active Expired - Lifetime
-
2004
- 2004-01-30 CN CNB2004800034661A patent/CN100465299C/en not_active Expired - Lifetime
- 2004-01-30 PL PL377834A patent/PL206109B1/en unknown
- 2004-01-30 EP EP04706710.3A patent/EP1592816B1/en not_active Expired - Lifetime
- 2004-01-30 ES ES04706710T patent/ES2831249T3/en not_active Expired - Lifetime
- 2004-01-30 UA UAA200508475A patent/UA87454C2/en unknown
- 2004-01-30 KR KR1020057014238A patent/KR101091021B1/en active IP Right Grant
- 2004-01-30 RU RU2005127577/02A patent/RU2341566C2/en active
- 2004-01-30 JP JP2006505664A patent/JP4528769B2/en not_active Expired - Lifetime
- 2004-01-30 BR BR0407236-7A patent/BRPI0407236A/en active IP Right Grant
- 2004-01-30 MX MXPA05008189A patent/MXPA05008189A/en active IP Right Grant
- 2004-01-30 HU HUE04706710A patent/HUE052206T2/en unknown
- 2004-01-30 US US10/544,206 patent/US20060144482A1/en not_active Abandoned
- 2004-01-30 WO PCT/FR2004/000209 patent/WO2004079022A1/en active Search and Examination
- 2004-01-30 CA CA2514736A patent/CA2514736C/en not_active Expired - Lifetime
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- 2005-07-25 ZA ZA200505968A patent/ZA200505968B/en unknown
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101781739A (en) * | 2010-03-18 | 2010-07-21 | 武汉钢铁(集团)公司 | Automobile cold-rolled dual-phase steel with tensile strength of 500 MPa |
| CN102115808A (en) * | 2010-11-17 | 2011-07-06 | 莱芜钢铁股份有限公司 | Ferrite region rolling temperature control system |
| CN102115808B (en) * | 2010-11-17 | 2013-04-24 | 山东钢铁股份有限公司 | Ferrite region rolling temperature control system |
| CN103952523A (en) * | 2014-04-15 | 2014-07-30 | 东北大学 | Continuous annealing method of martensitic ferritic dual-phase steel cold-rolled strip |
| CN103952523B (en) * | 2014-04-15 | 2016-01-20 | 东北大学 | A kind of continuous annealing method of martensite ferrite dual phase steel cold rolled sheet |
| CN105401071A (en) * | 2015-12-22 | 2016-03-16 | 武汉钢铁(集团)公司 | Galvanized dual-phase steel for 500 MPa class car and production method |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2004079022A1 (en) | 2004-09-16 |
| BRPI0407236A (en) | 2006-01-31 |
| FR2850671B1 (en) | 2006-05-19 |
| CN100465299C (en) | 2009-03-04 |
| CA2514736C (en) | 2012-12-04 |
| JP4528769B2 (en) | 2010-08-18 |
| UA87454C2 (en) | 2009-07-27 |
| ES2831249T3 (en) | 2021-06-08 |
| HUE052206T2 (en) | 2021-04-28 |
| CA2514736A1 (en) | 2004-09-16 |
| RU2341566C2 (en) | 2008-12-20 |
| JP2006520431A (en) | 2006-09-07 |
| KR20050095782A (en) | 2005-09-30 |
| US20060144482A1 (en) | 2006-07-06 |
| MXPA05008189A (en) | 2005-10-05 |
| KR101091021B1 (en) | 2011-12-09 |
| PL206109B1 (en) | 2010-07-30 |
| ZA200505968B (en) | 2006-06-28 |
| FR2850671A1 (en) | 2004-08-06 |
| RU2005127577A (en) | 2006-02-10 |
| EP1592816A1 (en) | 2005-11-09 |
| PL377834A1 (en) | 2006-02-20 |
| EP1592816B1 (en) | 2020-10-14 |
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