CN109023106A - A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof - Google Patents
A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof Download PDFInfo
- Publication number
- CN109023106A CN109023106A CN201811116059.1A CN201811116059A CN109023106A CN 109023106 A CN109023106 A CN 109023106A CN 201811116059 A CN201811116059 A CN 201811116059A CN 109023106 A CN109023106 A CN 109023106A
- Authority
- CN
- China
- Prior art keywords
- cold rolling
- dip galvanizing
- hot dip
- steel
- multiphase steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/26—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; 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
- 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
Abstract
The present invention relates to a kind of cold rolling hot dip galvanizing Multiphase Steels and preparation method thereof, and chemical component weight percentage is respectively as follows: C:0.08-0.12%, Si:0.3-0.6%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.015%, Al:0.1-0.4%, Cr:0.2-0.5%, Mo:0.1-0.4%, Nb:0.03-0.06%, Ti:0.03-0.06%, B:0.002-0.003%, surplus are Fe and inevitable impurity.The present invention, which passes through, utilizes above-mentioned reasonable alloying component system, determines matched reasonable process method therewith, produces producing line according to conventional annealing, obtains 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel.The present invention improves the yield strength and welding performance of material, buckling performance and reaming performance also increase accordingly under the premise of guaranteeing that cold rolling hot dip galvanizing Multiphase Steel tensile strength reaches 1000MPa grades.
Description
Technical field
The present invention relates to iron and steel smelting technology field, in particular to a kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof.
Background technique
Recently as the needs of development and the energy-saving and emission-reduction of automobile industry, automobile steel gradually develops to high strength steel,
International automobile is up to 50% with the super-high strength steel ratio in steel alliance FSV project being more than 1000MPa.1000MPa or more is high-strength
Steel removes common dual phase steel, further includes martensite steel, Multiphase Steel, third generation high-strength steel etc..
Traditional high-strength steel is mainly dual phase steel, is organized mainly by the softer higher geneva of ferrite matrix and intensity
The performance characteristics of body composition, this tissue are lower yield tensile ratio, higher intensity etc., are appropriate for the life of stamping part
It produces；But since ferrite and the soft or hard phase difference of hardness of martensite are larger, bending property and reaming performance are lower.
Summary of the invention
In order to solve the above technical problems, the present invention provides a kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof, make cold
It rolls hot galvanizing Multiphase Steel and improves buckling performance and reaming performance on the basis of meeting intensity requirement.
In order to achieve the above object, the present invention adopts the following technical scheme: a kind of cold rolling hot dip galvanizing Multiphase Steel, including it is as follows
The chemical component of weight percent: C:0.08-0.12%, Si:0.3-0.6%, Mn:2.0-2.5%, P :≤0.02%, S :≤
0.015%, Al:0.1-0.4%, Cr:0.2-0.5%, Mo:0.1-0.4%, Nb:0.03-0.06%, Ti:0.03-0.06%,
B:0.002-0.003%, surplus are Fe and inevitable impurity.
As a further preference, the Cr+Mo element content range is 0.3-0.7%.
As a further preference, the Nb+Ti element content range is 0.05-0.08%.
As a further preference, it is 20 that the internal microstructure of the cold rolling hot dip galvanizing Multiphase Steel, which includes: volume fraction,
~30% ferrite, 40~50% bainites and 20~30% martensites.
As a further preference, tensile strength >=980MPa of the cold rolling hot dip galvanizing Multiphase Steel, yield strength >=
700MPa, elongation percentage A80 >=6%.
Another object of the present invention is to provide the preparation methods of above-mentioned cold rolling hot dip galvanizing Multiphase Steel, include the following steps:
(1) molten steel containing above-mentioned chemical component is cast as steel billet；
(2) steel billet obtains hot rolled plate by hot rolling；The steel billet is heated, is obtained using roughing, finish rolling
Then hot rolled plate will coil into hot rolled coil after hot rolled plate cooling；
(3) hot rolled coil obtains chill strip through cold rolling；
(4) the chill strip handles to obtain cold rolling hot dip galvanizing Multiphase Steel finished product by continuous zinc coating annealing process.
As a further preference, in the step (2), the heating temperature of the steel billet is 1120-1300 DEG C；Its hot rolling
860-920 DEG C of finishing temperature；600-660 DEG C of its hot-rolling coiling temperature.
As a further preference, in the step (3), the cold rolling reduction ratio of the steel billet is 55%-75%.
As a further preference, in the step (4), the continuous zinc coating annealing process includes:
The chill strip is preheated to 220 DEG C；790 DEG C -820 DEG C are heated to 1-3 DEG C/s rate again and are kept the temperature；
By the strip after the heat preservation with the slow cooling of 10~20 DEG C/s cooling rate to 690 DEG C -720 DEG C；
Strip after the slow cooling is but cooled to zinc-plated temperature 450-460 through height is hydrogen-cooled with 20~40 DEG C/s cooling rate fastly
DEG C, zinc-plated processing is carried out after timeliness 20-50s；
The strip is air-cooled after zinc-plated after zinc-plated is cooled to 410-430 DEG C；It is then cooled to room temperature.
As a further preference, the chill strip is after the processing of continuous zinc coating annealing process further include: will be described
Strip batches to obtain finished product after finishing, and finishing elongation percentage is 0.3%-0.5%.
The beneficial effects of the present invention are: the present invention, which passes through, utilizes above-mentioned reasonable alloying component system, determine therewith therewith
The reasonable process method to match produces producing line according to conventional annealing, obtains 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel.This
Invention is added appropriate Cr, Mo member and is usually protected under the premise of guaranteeing that cold rolling hot dip galvanizing Multiphase Steel tensile strength reaches 1000MPa grades
Harden ability is demonstrate,proved, guarantees the tensile strength of material；It adds appropriate Nb, Ti element and carries out crystal grain refinement and precipitation strength, thinning microstructure
Structure, while reinforced ferrite generate ferrite+bainite+martensite heterogeneous structure, improve the yield strength and welding of material
Performance, buckling performance and reaming performance also increase accordingly.
Detailed description of the invention
By reading the following detailed description of the preferred embodiment, various other advantages and benefits are common for this field
Technical staff will become clear.The drawings are only for the purpose of illustrating a preferred embodiment, and is not considered as to the present invention
Limitation.
Fig. 1 is optical microstructure's photo of the 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel of preparation of the embodiment of the present invention.
Fig. 2 is that the precipitated phase of the 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel of preparation of the embodiment of the present invention transmits microscopic structure
Photo.
Specific embodiment
The embodiment of the present invention solves existing automobile by providing a kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof
Steel bending property and the lower defect of reaming performance.
Complex phase steel microscopic structure is mainly ferrite/bainite, includes a certain amount of martensite, crystal grain is tiny, tension
Intensity is higher.This steel energy absorption capability, good mechanical property, processability and welding performance with higher, simultaneously
Have the characteristics that bending property and reaming performance height etc., meets the production of flange bending and forming part.
In order to solve drawbacks described above, the main thought of the embodiment of the present invention is:
Cold rolling hot dip galvanizing Multiphase Steel of the embodiment of the present invention, the chemical component including following weight percent: C:0.08-
0.12%, Si:0.3-0.6%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.015%, Al:0.1-0.4%, Cr:0.2-
0.5%, Mo:0.1-0.4%, Nb:0.03-0.06%, Ti:0.03-0.06%, B:0.002-0.003%, surplus is for Fe and not
Evitable impurity.
Detailed description are as follows for above-mentioned main alloy element effect and restriction range:
Carbon C: carbon is most important solution strengthening element in Multiphase Steel, stable austenite in annealing process, thus
Enough martensite volumes are obtained in cooling procedure to guarantee the intensity of Multiphase Steel, but carbon content is excessively high can reduce forming property and weldering
Performance is connect, therefore the present invention uses carbon content for 0.08-0.12%.
Silicon Si: element silicon can expand two-phase section, while silicon is solid-solution in ferrite that ferrite intensity can be improved, and make simultaneously
Carbon spread improves austenite harden ability into austenite.But element silicon is excessively high to will lead to the increase of bar hot rolling surface red rust defect, reduces
Finished surface quality, therefore the present invention uses silicone content for 0.3-0.6%.
Manganese Mn: manganese plays solution strengthening effect in steel, at the same can stable austenite, improve the intensity of steel plate after quenching.
Manganese content is excessively high to hinder ferrite transformation, while being easy to be segregated, and MnS field trash is generated in conjunction with element sulphur, deteriorates the property of steel
Energy.In consideration of it, the content of manganese is set between 2.0% to 2.5%.
Phosphorus P and sulphur S: p and s are the harmful elements in steel.Phosphorus is easy in grain boundaries segregation, the serious plasticity for damaging steel plate
And toughness；Sulphur forms plastic occluded foreignsubstance manganese sulfide with chemical combination such as manganese in steel, unfavorable to the horizontal plastic property and toughness of steel, therefore sulphur
Content should be low as far as possible.Therefore present invention control phosphorus content is less than or equal to 0.02%, and sulfur content is less than or equal to
0.015%.
Aluminium Al: aluminium mainly plays deoxidation in steel-making, to two-phase section to act on Si similar.In addition, proper content
Aluminium can also accelerate bainite transformation, and can hinder the formation of carbide, and carbon is retained in the melt, to promote austenite
Stablize.For this purpose, the content of aluminium is set between 0.1% to 0.4%.
Chromium Cr: chromium can significantly improve the harden ability of steel, guarantee the intensity of material.Chromium enhances while ferrite formation
The formation of retained austenite, thus, the content of chromium is not less than 0.2%, otherwise influences the harden ability of steel；Also it should not be greater than
0.5%, to ensure cost economy.
Molybdenum Mo: the effect of molybdenum mainly improves the temper resistance of martensite, enough improves quenching for steel with Cr element binding energy
Permeability, while crystal grain can be refined, and improve the stability of austenite, improve the strength of materials.Therefore the present invention uses molybdenum element
Content is 0.1-0.4%.
Niobium Nb: niobium is strong carbon compound formation element, can delay hot rolling Austenite Recrystallization Process.Niobium member simultaneously
Element generates NbC in conjunction with carbon and is precipitated, and can play the effect of precipitation strength, improve the yield strength of material.The present invention adopts
It is 0.03-0.06% with niobium element content.
Titanium Ti: the effect of titanium is similar to niobium.Titanium can form the compound of titanium with nitrogen, carbon and sulphur.Titanium contains in control steel
Amount forms niobium carbonitrides Second Phase Precipitation, can provide refined crystalline strengthening and precipitating reinforcing effect.The present invention uses titanium elements content
For 0.03-0.06%.
Boron: be added trace B can significantly improve material harden ability, while improving the strength of materials to other performances without
Influence or influence very little.But boron content is larger to easily cause brittleness.Therefore the present invention uses boron content for 0.002-
0.003%.
In certain embodiments of the present invention, Cr+Mo constituent content preferred scope is 0.3-0.7%.Add appropriate Cr, Mo
Member usually guarantees harden ability.
Nb+Ti is the microalloy element of addition, and tiny NbC, TiC precipitated phase can be precipitated in ferrite matrix, is carried out
Crystal grain refinement and precipitation strength, thinning microstructure structure, while reinforced ferrite improve the yield strength of material, guarantee martensite
With bainite on ferrite matrix Dispersed precipitate.
In certain embodiments of the present invention, Nb+Ti constituent content preferred scope is 0.05-0.08%, too low to mention
It is excessively high for adequately refining and strengthening effect, cause precipitated phase excessive, reduces precipitating reinforcing effect.
In certain embodiments of the present invention, the internal microstructure of the cold rolling hot dip galvanizing Multiphase Steel is ferrite+shellfish
Family name's body+martensite.
Further, the internal microstructure of the cold rolling hot dip galvanizing Multiphase Steel is 20~30% iron element by volume fraction
Body, 40~50% bainites and 20~30% martensites composition.The organization type of the ratio can guarantee that the cold rolling hot dip galvanizing is multiple
Phase steel improves buckling performance on the basis of meeting intensity requirement.
The embodiment of the present invention can produce producing line by conventional continuous annealing and cold rolling hot dip galvanizing Multiphase Steel is prepared, such as:
Include the following steps:
(1) molten steel containing above-mentioned chemical component is cast as steel billet；
(2) steel billet obtains hot rolled plate by hot rolling；The steel billet is heated, is obtained using roughing, finish rolling
Then hot rolled plate will coil into hot rolled coil after hot rolled plate cooling；
(3) hot rolled coil obtains chill strip through cold rolling；
(4) the chill strip handles to obtain cold rolling hot dip galvanizing Multiphase Steel finished product by continuous zinc coating annealing process.
The embodiment of the present invention passes through the proportion design of mentioned component and selects corresponding preparation method, and in method
Parameter is adjusted, and has obtained buckling performance and reaming cold rolling hot dip galvanizing Multiphase Steel of good performance.
In order to which above and other purpose, feature and the advantage of the present invention can be clearer and more comprehensible, several implementations are cited below particularly
Example, to illustrate cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof of the present invention.
A kind of method producing 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel provided in an embodiment of the present invention, including it is following several
A step:
Step S1: molten steel is passed through into converter smelting, slab is obtained using continuous casting mode；Practical chemical component is as shown in table 1.
1 1000MPa complex phase steel chemical composition (wt%) of table
Step S2: the slab is heated, and hot rolled plate is obtained using roughing, finish rolling, then by the hot rolled plate
Section cooling is carried out, coils into hot rolled coil after cooling；
Specifically, the slab heating temperature is 1120-1300 DEG C；860-920 DEG C of the hot rolling finishing temperature；The heat
Roll 600-660 DEG C of coiling temperature.
Step S3: the hot rolled coil is obtained into chill strip by cold rolling；When the hot rolled coil passes through cold rolling, under cold rolling
Rate is 55%-75%, in favor of the progress of cold-rolling process.Hot rolling and Cold-rolling Parameters embodiment are shown in Table 2.
2 1000MPa Multiphase Steel hot rolling of table and cold-rolling process embodiment
Step S4: the chill strip handles to obtain cold rolling hot dip galvanizing Multiphase Steel finished product by continuous zinc coating annealing process.
Specifically, the chill strip is preheated to 220 DEG C；
Chill strip after the preheating reheats and the temperature kept the temperature is 790 DEG C -820 DEG C, soaking temperature 790-
820℃；
By the strip slow cooling after heat preservation to 690 DEG C -720 DEG C, cooling rate is 10-20 DEG C/s.Slow cooling temperature can promote iron plain
C is enriched with into austenite in body, purifies harden ability that is ferritic while improving austenite.Cooling rate can adjust ferrite
Ratio, obtain different mechanical properties；
Strip after the slow cooling is but cooled to zinc-plated temperature 450-460 through height is hydrogen-cooled with 20~40 DEG C/s cooling rate fastly
DEG C, zinc-plated processing is carried out after timeliness 20-50s.The strip is air-cooled after zinc-plated after zinc-plated is cooled to 410-430 DEG C；With
After be cooled to room temperature, finishing elongation percentage be 0.3%-0.5%.Rapid cooling temperature guarantees the formation of bainite and martensite, guarantees material
The intensity of material.The content of rapid cooling rate adaptation bainite and martensite, obtains different mechanical properties.Finishing elongation percentage can change
Kind surface roughness, while improving material yield strength.Table 3 is 1000MPa hot galvanizing Multiphase Steel continuous hot galvanizing annealing process
Embodiment parameter.
3 1000MPa Multiphase Steel continuous hot galvanizing annealing process embodiment of table
1000MPa grade cold rolling hot dip galvanizing Multiphase Steel provided by the above embodiment is tested for the property, data see the table below 4.
Table 4
The disproportional elongation of Rp0.2 representing sample guage section reaches stress when original gauge length 0.2%；
Stretching experiment standard is GB/T228-2002.
Fig. 1 is the microstructure picture for the cold rolling hot dip galvanizing Multiphase Steel that the embodiment of the present invention 1 provides.Use picric acid inclined
Sodium bisulfite solution corrosion, wherein grey is ferrite, and black is bainite structure, and brilliant white is horse island (MA) difficult to understand.From figure
In as can be seen that microscopic structure of the embodiment of the present invention in crystallite dimension it is tiny, ferrite can mention in microscopic structure for Multiphase Steel
For certain ductile deformation；The presence on the island certain proportion MA can provide higher intensity for Multiphase Steel；Appropriate bainite is deposited
It can be used as the transitional face between soft phase ferrite and hard phase martensite, can be effectively reduced between ferrite and martensite
Difference of hardness, further increase the buckling performance and reaming performance of Multiphase Steel.It should be noted that provided in an embodiment of the present invention
There is the presence (Fig. 2) of a certain amount of Nb, Ti precipitated phase in tensile strength 1000MPa grade cold rolling hot dip galvanizing Multiphase Steel, it is strong by fine grain
Change and precipitation strength further improves the bending and forming ability of material.
Technical solution in above-mentioned the embodiment of the present application, at least have the following technical effects or advantages:
1000MP grades of Multiphase Steel provided by the present application adds the members such as a certain amount of Cr, Mo, B to meet zinc-plated production requirement
Element improves the harden ability of material, guarantees the tensile strength of material；The microalloy elements such as a certain amount of Nb, Ti are added simultaneously, are obtained
Nano-scale precipitated phase carries out refined crystalline strengthening and precipitation strength, improves the yield strength of material, while making bainite, martensite
Dispersed precipitate improves the buckling performance and reaming performance of material.
Although preferred embodiments of the present invention have been described, it is created once a person skilled in the art knows basic
Property concept, then additional changes and modifications may be made to these embodiments.So it includes excellent that the following claims are intended to be interpreted as
It selects embodiment and falls into all change and modification of the scope of the invention.Obviously, those skilled in the art can be to the present invention
Carry out various modification and variations without departing from the spirit and scope of the present invention.If in this way, these modifications and changes of the present invention
Within the scope of the claims of the present invention and its equivalent technology, then the present invention is also intended to encompass these modification and variations and exists
It is interior.
Claims (10)
1. a kind of cold rolling hot dip galvanizing Multiphase Steel, it is characterised in that: the chemical component including following weight percent: C:0.08-
0.12%, Si:0.3-0.6%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.015%, Al:0.1-0.4%, Cr:0.2-
0.5%, Mo:0.1-0.4%, Nb:0.03-0.06%, Ti:0.03-0.06%, B:0.002-0.003%, surplus is for Fe and not
Evitable impurity.
2. cold rolling hot dip galvanizing Multiphase Steel according to claim 1, it is characterised in that: the Cr+Mo element content range is
0.3-0.7%.
3. cold rolling hot dip galvanizing Multiphase Steel according to claim 1, it is characterised in that: the Nb+Ti element content range is
0.05-0.08%.
4. cold rolling hot dip galvanizing Multiphase Steel according to claim 1, it is characterised in that: the cold rolling hot dip galvanizing Multiphase Steel it is interior
Portion's microscopic structure includes: that volume fraction is 20~30% ferrites, 40~50% bainites and 20~30% martensites.
5. cold rolling hot dip galvanizing Multiphase Steel according to claim 1, it is characterised in that: the cold rolling hot dip galvanizing Multiphase Steel resists
Tensile strength >=980MPa, yield strength >=700MPa, elongation percentage A80 >=6%.
6. the preparation method of cold rolling hot dip galvanizing Multiphase Steel as described in claim any one of 1-5, it is characterised in that: including walking as follows
It is rapid:
(1) molten steel containing above-mentioned chemical component is cast as steel billet；
(2) steel billet obtains hot rolled plate by hot rolling；The steel billet is heated, obtains hot rolling using roughing, finish rolling
Then plate will coil into hot rolled coil after hot rolled plate cooling；
(3) hot rolled coil obtains chill strip through cold rolling；
(4) the chill strip handles to obtain cold rolling hot dip galvanizing Multiphase Steel finished product by continuous zinc coating annealing process.
7. the preparation method of cold rolling hot dip galvanizing Multiphase Steel according to claim 6, it is characterised in that: in the step (2), institute
The heating temperature for stating steel billet is 1120-1300 DEG C；Hot rolling finishing temperature is 860-920 DEG C；Hot-rolling coiling temperature is 600-660
℃。
8. the preparation method of cold rolling hot dip galvanizing Multiphase Steel according to claim 6, it is characterised in that: in the step (3), institute
The cold rolling reduction ratio for stating steel billet is 55%-75%.
9. the preparation method of cold rolling hot dip galvanizing Multiphase Steel according to claim 6, it is characterised in that: in the step (4), institute
Stating continuous zinc coating annealing process includes:
The chill strip is preheated to 220 DEG C；790 DEG C -820 DEG C are heated to 1-3 DEG C/s rate again and are kept the temperature；
By the strip after the heat preservation with the slow cooling of 10~20 DEG C/s cooling rate to 690 DEG C -720 DEG C；
Strip after the slow cooling is but cooled to 450-460 DEG C of zinc-plated temperature through height is hydrogen-cooled with 20~40 DEG C/s cooling rate fastly,
Zinc-plated processing is carried out after timeliness 20-50s；
The strip is air-cooled after zinc-plated after zinc-plated is cooled to 410-430 DEG C；It is then cooled to room temperature.
10. the preparation method of cold rolling hot dip galvanizing Multiphase Steel according to claim 6, it is characterised in that: the chill strip warp
After crossing the processing of continuous zinc coating annealing process further include: batch the strip after finishing to obtain finished product, finishing elongation percentage is
0.3%-0.5%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811116059.1A CN109023106A (en) | 2018-09-25 | 2018-09-25 | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201811116059.1A CN109023106A (en) | 2018-09-25 | 2018-09-25 | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN109023106A true CN109023106A (en) | 2018-12-18 |
Family
ID=64617828
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201811116059.1A Pending CN109023106A (en) | 2018-09-25 | 2018-09-25 | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109023106A (en) |
Cited By (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109594020A (en) * | 2018-12-28 | 2019-04-09 | 首钢集团有限公司 | A kind of tensile strength 1000MPa grades of cold rolling Multiphase Steels and preparation method thereof |
| CN109778062A (en) * | 2018-12-28 | 2019-05-21 | 首钢集团有限公司 | A kind of tensile strength 1200MPa grades of cold rolling Multiphase Steels and preparation method thereof |
| CN109926458A (en) * | 2019-03-19 | 2019-06-25 | 首钢集团有限公司 | A kind of Thin Strip Steel that sea surface oil slick is stable and its production method |
| CN110004360A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of yield strength is not less than 650MPa grades of bendings cold rolling hard steel band and manufacturing methods |
| CN110129668A (en) * | 2019-04-25 | 2019-08-16 | 首钢集团有限公司 | A kind of 1000MPa grades of alloyed zinc hot dip galvanized Multiphase Steel and preparation method thereof |
| CN110551942A (en) * | 2019-09-05 | 2019-12-10 | 首钢集团有限公司 | 650 MPa-grade hot-rolled dual-phase steel for automobile rim and preparation method thereof |
| CN110983198A (en) * | 2019-12-16 | 2020-04-10 | 首钢集团有限公司 | Alloying hot galvanizing dual-phase steel and preparation method thereof |
| CN111008477A (en) * | 2019-12-06 | 2020-04-14 | 马鞍山钢铁股份有限公司 | Method for adjusting technological parameters based on mechanical properties of cold-rolled galvanized strip steel |
| CN111926247A (en) * | 2020-07-13 | 2020-11-13 | 首钢集团有限公司 | 800 MPa-grade cold-rolled hot-galvanized complex-phase steel and preparation method thereof |
| CN111979488A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade alloying hot-dip galvanized DH steel and preparation method thereof |
| CN112126852A (en) * | 2020-09-03 | 2020-12-25 | 唐山钢铁集团有限责任公司 | 980 MPa-grade cold-rolled complex phase steel for roll forming and preparation method thereof |
| CN114921726A (en) * | 2022-05-27 | 2022-08-19 | 武汉钢铁有限公司 | Low-cost high-yield-ratio cold-rolled hot-galvanized ultrahigh-strength steel and production method thereof |
| CN115558844A (en) * | 2022-09-15 | 2023-01-03 | 首钢集团有限公司 | 1180 MPa-grade steel, galvanized steel, preparation method of galvanized steel and automobile accessory |
| CN115612816A (en) * | 2022-09-30 | 2023-01-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for preparing complex phase steel and steel plating plate for hot forming from boron-containing steel |
| CN116043119A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | Easily-welded ultra-high reaming performance 800 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
| CN116043121A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 800 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043120A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 1000 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043118A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | Ultra-high reaming performance 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104831177A (en) * | 2015-05-11 | 2015-08-12 | 首钢总公司 | Cold-rolling hot-galvanizing double-phase steel and preparation method thereof |
| CN108486500A (en) * | 2018-05-15 | 2018-09-04 | 首钢集团有限公司 | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof |
-
2018
- 2018-09-25 CN CN201811116059.1A patent/CN109023106A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104831177A (en) * | 2015-05-11 | 2015-08-12 | 首钢总公司 | Cold-rolling hot-galvanizing double-phase steel and preparation method thereof |
| CN108486500A (en) * | 2018-05-15 | 2018-09-04 | 首钢集团有限公司 | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof |
Cited By (29)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109594020B (en) * | 2018-12-28 | 2020-07-24 | 首钢集团有限公司 | Cold-rolled complex phase steel with tensile strength of 1000MPa and preparation method thereof |
| CN109778062A (en) * | 2018-12-28 | 2019-05-21 | 首钢集团有限公司 | A kind of tensile strength 1200MPa grades of cold rolling Multiphase Steels and preparation method thereof |
| CN109594020A (en) * | 2018-12-28 | 2019-04-09 | 首钢集团有限公司 | A kind of tensile strength 1000MPa grades of cold rolling Multiphase Steels and preparation method thereof |
| CN109778062B (en) * | 2018-12-28 | 2020-09-15 | 首钢集团有限公司 | Cold-rolled complex phase steel with tensile strength of 1200MPa and preparation method thereof |
| CN109926458A (en) * | 2019-03-19 | 2019-06-25 | 首钢集团有限公司 | A kind of Thin Strip Steel that sea surface oil slick is stable and its production method |
| CN109926458B (en) * | 2019-03-19 | 2020-09-15 | 首钢集团有限公司 | Thin strip steel with stable surface oil film and production method thereof |
| CN110004360A (en) * | 2019-03-29 | 2019-07-12 | 山东钢铁集团日照有限公司 | A kind of yield strength is not less than 650MPa grades of bendings cold rolling hard steel band and manufacturing methods |
| CN110129668A (en) * | 2019-04-25 | 2019-08-16 | 首钢集团有限公司 | A kind of 1000MPa grades of alloyed zinc hot dip galvanized Multiphase Steel and preparation method thereof |
| CN110551942A (en) * | 2019-09-05 | 2019-12-10 | 首钢集团有限公司 | 650 MPa-grade hot-rolled dual-phase steel for automobile rim and preparation method thereof |
| CN111008477A (en) * | 2019-12-06 | 2020-04-14 | 马鞍山钢铁股份有限公司 | Method for adjusting technological parameters based on mechanical properties of cold-rolled galvanized strip steel |
| CN111008477B (en) * | 2019-12-06 | 2023-03-24 | 马鞍山钢铁股份有限公司 | Method for adjusting technological parameters based on mechanical properties of cold-rolled galvanized strip steel |
| CN110983198A (en) * | 2019-12-16 | 2020-04-10 | 首钢集团有限公司 | Alloying hot galvanizing dual-phase steel and preparation method thereof |
| CN111926247A (en) * | 2020-07-13 | 2020-11-13 | 首钢集团有限公司 | 800 MPa-grade cold-rolled hot-galvanized complex-phase steel and preparation method thereof |
| CN112126852A (en) * | 2020-09-03 | 2020-12-25 | 唐山钢铁集团有限责任公司 | 980 MPa-grade cold-rolled complex phase steel for roll forming and preparation method thereof |
| CN111979488B (en) * | 2020-09-07 | 2021-11-16 | 鞍钢股份有限公司 | 780 MPa-grade alloying hot-dip galvanized DH steel and preparation method thereof |
| CN111979488A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade alloying hot-dip galvanized DH steel and preparation method thereof |
| CN114921726A (en) * | 2022-05-27 | 2022-08-19 | 武汉钢铁有限公司 | Low-cost high-yield-ratio cold-rolled hot-galvanized ultrahigh-strength steel and production method thereof |
| CN114921726B (en) * | 2022-05-27 | 2023-10-20 | 武汉钢铁有限公司 | Low-cost high-yield-ratio cold-rolled hot-dip galvanized ultrahigh-strength steel and production method thereof |
| CN115558844A (en) * | 2022-09-15 | 2023-01-03 | 首钢集团有限公司 | 1180 MPa-grade steel, galvanized steel, preparation method of galvanized steel and automobile accessory |
| CN115612816A (en) * | 2022-09-30 | 2023-01-17 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for preparing complex phase steel and steel plating plate for hot forming from boron-containing steel |
| CN115612816B (en) * | 2022-09-30 | 2024-02-02 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for preparing complex phase steel and steel plating plate for thermoforming from boron-containing steel |
| CN116043120A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 1000 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043118A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | Ultra-high reaming performance 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
| CN116043121A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | 800 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043121B (en) * | 2023-01-19 | 2023-10-24 | 鞍钢股份有限公司 | 800 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043118B (en) * | 2023-01-19 | 2023-10-27 | 鞍钢股份有限公司 | Ultra-high reaming performance 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
| CN116043119B (en) * | 2023-01-19 | 2023-10-27 | 鞍钢股份有限公司 | Easily-welded ultra-high reaming performance 800 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
| CN116043120B (en) * | 2023-01-19 | 2023-10-27 | 鞍钢股份有限公司 | 1000 MPa-grade cold-rolled complex phase steel with excellent formability and preparation method thereof |
| CN116043119A (en) * | 2023-01-19 | 2023-05-02 | 鞍钢股份有限公司 | Easily-welded ultra-high reaming performance 800 MPa-grade hot dip galvanized complex phase steel and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109023106A (en) | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof | |
| CN108486500A (en) | A kind of cold rolling hot dip galvanizing Multiphase Steel and preparation method thereof | |
| CN106119702B (en) | A kind of high reaming steel of 980MPa grades of hot-rolled high-strength and its manufacturing method | |
| CN107119228B (en) | A kind of 700~800MPa of tensile strength grades of hot rolling high-strength light dual phase steels and its manufacturing method | |
| CN109097705A (en) | A kind of 800MPa grade cold rolling hot dip galvanizing dual phase steel and its production method | |
| CN100439543C (en) | Hot-rolled super-strength martensitic steel and method for manufacturing same | |
| CN103339280B (en) | Excellent processability also has high strength cold rolled steel plate and the manufacture method thereof of high yield ratio | |
| CN102586688B (en) | A kind of dual phase sheet steel and manufacture method thereof | |
| CN104520449B (en) | A kind of method for producing hot rolled strip and the steel band thus produced | |
| CN103842540A (en) | Hot-dip galvanized steel sheet and method for producing same | |
| WO2013075473A1 (en) | Steel plate with ultra-high strength and abrasion resistance, and manufacturing process thereof | |
| CN107881430A (en) | A kind of tensile strength 600MPa levels hot-rolled dual-phase steel and its manufacture method | |
| CN103380217A (en) | Hot rolled flat steel product produced from a complex phase steel, and method for producing same | |
| KR20180095536A (en) | High Strength Galvanized Steel Strip | |
| CN107699791B (en) | 900MPa grades high cold-bending property low alloy high strength steel plate and preparation method thereof | |
| CN107326276B (en) | A kind of 500~600MPa of tensile strength grades of hot rolling high-strength light dual phase steels and its manufacturing method | |
| CN109055651A (en) | A method of 600MPa grades of carriage body steel of hot rolling thin gauge are produced completely without head bar strip continuous casting and rolling flow path based on ESP | |
| CN109355567A (en) | A kind of low cost Q390D steel plate and preparation method thereof | |
| CN109957717A (en) | A kind of precision stamping hot rolled steel plate containing B and its manufacturing method | |
| CN112322976A (en) | Rare earth wear-resistant steel NM400 coiled plate with excellent low-temperature-resistant toughness and production method thereof | |
| CN103898417A (en) | Non-tempered low-crack sensitivity steel strip and preparation method thereof | |
| CN109913763A (en) | The good inexpensive cold-rolled biphase steel of 1000MPa grades of cold-forming properties and its manufacturing method | |
| CN106636911A (en) | 900MPa hot rolling sheet steel formed by directly rolling sheet billets and manufacturing method thereof | |
| CN105925905B (en) | 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems and its production method | |
| CN107904509A (en) | A kind of Thin Specs 1180MPa grades of dual phase steels and its processing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20181218 |
|
| RJ01 | Rejection of invention patent application after publication |