CN103882320B - Stretch flangeability and the excellent high strength cold rolled steel plate of spot weldability and manufacture method thereof - Google Patents
Stretch flangeability and the excellent high strength cold rolled steel plate of spot weldability and manufacture method thereof Download PDFInfo
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Abstract
The invention provides a kind of stretch flangeability and the excellent high strength cold rolled steel plate of spot weldability and manufacture method thereof, this steel plate chemical composition: C0.03% ~ 0.15%, Si0.30 ~ 0.10%, Mn1.20% ~ 2.20%, P≤0.015%, S≤0.010%, Al0.02% ~ 0.15%, N≤0.005%, Cr0.20% ~ 0.60%, Nb 0.010% ~ 0.060%, V0.030% ~ 0.100%, Ca0.0007% ~ 0.0050%, and meeting 1.6%≤Mn+2Nb+V≤2.3%, surplus is Fe and inevitable impurity.Its manufacture method hot continuous rolling finish rolling start rolling temperature 1000 ~ 1100 DEG C, finishing temperature 890 ~ 950 DEG C, under pickling and cold-rolling, rate is 60 ~ 80%, quickly cools down two-stage cooling after using first Slow cooling after annealing insulation.Finally giving tensile strength good in more than 800MPa, intensity and ductility coupling, stretch flangeability and spot weldability are excellent.
Description
Technical field
The invention belongs to automobile cold-rolled high intensity thin slab technique field, particularly relate to a kind of stretch flange formability
Property and the excellent high strength cold rolled steel plate of spot weldability and manufacture method thereof.
Background technology
In recent years, along with the fast development of auto industry, automobile as the daily vehicles to people
Bring simultaneously easily, also become generation CO2, NOx and the primary pollution source of noise, it is therewith
And the environment come and energy problem are also increasingly subject to the great attention of people.In order to reduce oil consumption,
Save the energy, it is achieved sustainable development, promote automobile to develop to environment-friendly type, lightweight direction.
Two-phase (DP) steel, phase change induction plasticity (DP) steel, complex phase (CP) steel are developed at present
With twin crystal inducing plasticity (TWIP) steel, for frame member, reinforcement and the anti-collision energy absorption of automobile
On component.High strength steel plate needs to be spot welded into luggage after machine-shaping and joins, but due to armor plate strength
Raising necessarily cause Extending flange Perfor (reaming performance) and the reduction of spot welding characteristics, limit
The extensive application of these high-strength steel sheets.Therefore, it is desirable to these high-strength steel sheets have height
While intensity, have excellent higher ream forming and spot welding characteristics concurrently.
Patent " a kind of high-elongation and the twin crystal induction plastic steel of high hole expansibility and manufacture method thereof " (
Publication number CN102400036A) twin crystal inducing of a kind of high-elongation of announcing and high hole expansibility moulds
Property steel, in steel, Mn content is 10% ~ 20%, and carbon content is 0.3% ~ 0.7%, and the steel of this composition is led
Hot and magnetic difference, continuous casting and subsequent production difficulty are big, and production cost is high, by hot rolling in patent
After plate is cold rolling in static furnace 600 ~ 1000 DEG C insulation after with the cooling rate solution treatment more than 20 DEG C/s
, the elongation percentage of the steel plate obtained and hole expansibility are high, but can not get excellent spot welding characteristics.
Korean Patent " has high strength cold rolled steel plate and the galvanized steel plain sheet of superior workability and manufactures it
Method " (PCT/KR2008/004642), in steel in addition to basis and Sb element,
Also need to add in all multielements of Co, Mo, Ti, Nb, V and Ca one or both and more than, separately
Outward, possibly together with the N of 70 ~ 300PPm in steel, this alloy system undoubtedly add smelting difficulty and
Product cost.This steel by annealing or hot dip galvanizing annealing process obtain ferrite, bainite and
The complex tissue of retained austenite, the excellent processability of steel but not necessarily there is excellent spot weldability
Energy.
Patent " high strength cold rolled steel plate of excellent in bending workability " (publication number CN102260821A)
Disclose a kind of steel plate and be organized as full martensite or martensite adds very small amount ferrite, tensile strength
The cold-rolled steel sheet of the excellent in bending workability more than 880MPa, but for the hole expandability of steel plate and point
Weldering property is not made to consider.
Patent " high strength cold rolled steel plate of excellent in workability and manufacture method thereof " (publication number CN1021
40608A) propose the high strength cold rolled steel plate of a kind of excellent in workability, micro-group of its steel plate
It is woven to bainite, retained austenite and tempered martensite.For obtaining this complex tissue, patent
Have employed 930 ~ 960 DEG C of soaking, two-stage cooling adds the process route of tempering, and this technique needs 4
The multiple spot plate temperature control of individual temperature spot, actual operation is complicated, it addition, high temperature soak also close to
The limit of existing cold rolled continuous annealing stove, it is achieved industry quantity-produced probability is the least and right
The spot welding characteristics of steel plate is not made to consider.
Japan Patent " high-strength hot-dip zinc-coated steel sheet of excellent processability and manufacture method thereof " (PCT/JP
2008/069699) provide one and be organized as ferrite, martensite and retained austenite and tempering horse
The processability of family name's body and the excellent high-strength hot-dip zinc-coated steel sheet of shock resistance and manufacture method thereof,
Without reference to the spot welding characteristics that finished product is cold rolled annealed plate and steel plate.
In view of to high strength steel plate Extending flange Perfor (reaming performance) and the requirement of spot welding characteristics, answering
Should be by effectively controlling on the smelting composition of steel and production technology, it is achieved ferrite and returning in steel plate
Fire martensite coexists with a small amount of bainite structure, and coordinates soft phase and hard phase in steel plate tissue
Difference of hardness, to obtain the excellent high ream forming performance of high strength steel plate and spot welding characteristics.
Summary of the invention
It is an object of the invention to overcome the problems referred to above and not enough and provide the one can be in industry
Be easily manufactured tensile strength on continuous annealing production line at more than 800Mpa, stretch flangeability and
High strength cold rolled steel plate that spot weldability is excellent and manufacture method thereof.
The present invention to achieve these goals, controls to smelt composition, hot rolling, cold rolling and continuous annealing work
Skill parameter, it is ensured that the high intensity of steel plate, microscopic structure is that ferrite, tempered martensite add on a small quantity
The heterogeneous structure of bainite, and excellent stretch flangeability and spot weldability.
The present invention is achieved in that
Stretch flangeability and the excellent high strength cold rolled steel plate composition of spot weldability are as follows
: C:0.03% ~ 0.15%, Si:0.30% ~ 0.10%, Mn:1.20% ~ 2.20%, P :≤0.0
15%, S :≤0.010%, Al:0.02% ~ 0.15%, N :≤0.005%, Cr:0.20% ~ 0.
60%, Nb:0.010% ~ 0.060%, V:0.030% ~ 0.100%, Ca:0.0007% ~ 0.00
50%, and meet 1.6%≤Mn+2Nb+V≤2.3%, surplus is that Fe is inevitable with some other
Impurity.
As to further improvement of the present invention, its constituent is as follows:
C:0.06% ~ 0.11%, Si:0.50 ~ 0.70%, Mn:1.60% ~ 2.00%, P :≤0.010%
, S :≤0.008%, Al:0.050% ~ 0.100%, N :≤0.0035%, Cr:0.30% ~
0.50%, Nb:0.020% ~ 0.050%, V:0.050% ~ 0.080%, Ca:0.0010% ~ 0.00
30%, and meet 1.8%≤Mn+2Nb+V≤2.1%, surplus is that Fe is inevitable with some other
Impurity.
Steel grades control principle of the present invention is as follows:
C: be that austenite generates element, is at tissue Composite, improves intensity and ductility balanced having
Effect element.For ensure steel plate has after low-temperature transformation a certain amount of austenite be transformed into bainite and
Martensite, and do not reduce spot welding characteristics, in the present invention, carbon content control is 0.03% ~ 0.15%,
More preferably 0.06% ~ 0.11%.
Si: be the element of reinforced ferrite, promote carbon to austenite segregation, to solid solution carbon in ferrite
There are removing and purification, the generation of thick carbide during to avoid gap solution strengthening and to cool down
, it is favorably improved the ductility of steel, but for avoiding Si too high levels to cause surface of steel plate to produce
Raw red rust, Si of the present invention controls 0.30% ~ 0.10%, and more preferably 0.50% ~ 0.70%.
Mn: belong to expansion austenite phase field, the element of stable austenite, austenite can be effectively improved
The quenching degree on island, thus after can reducing steel plate middle temperature transformation, remaining austenite is transformed into geneva
Cooldown rate necessary to body, and play the effect of solution strengthening and fining ferrite grains.High
Fe content easily causes cementite, pearlite and bainite to be main banded structure, and affects
The spot welding characteristics of steel plate.Mn content of the present invention controls 1.20% ~ 2.20%, and more preferably 1.60% ~ 2
.00%。
Al:Al is main deoxidizer, and Al can also form AlN precipitation simultaneously, plays certain refinement
Crystal grain effect.In steel, Al is when deoxidation is added, and unsuitable too low, otherwise Mn, Si etc. are thick
Oxide disperse in a large number in steel, deteriorate steel, but too much tufted aluminium oxide inclusion increase
Many, make the ductility of steel and weldability be deteriorated, steel-making can be affected again and continuous casting produces, the present invention
Middle Al content controls 0.02% ~ 0.15%, and more preferably 0.050% ~ 0.100%.
Cr: middle carbide, significantly improves the quenching degree of steel, can strongly postpone pearlite
Change and bainite transformation, the supercool ability of increase austenite, thus thinning microstructure, play strong
Change effect.It addition, the solution strengthening ability that Cr element is in steel is little, too much interpolation can reduce a little
Weldering performance.The content of Cr of the present invention controls 0.20% ~ 0.60%, and more preferably 0.30% ~ 0.50%.
Nb, V: for improving the element of intensity crystal grain thinning.Adding Nb and V element in steel, N can be
Steel becomes precipitated phase prior to C-shaped so that there is refining grain size and keep the effect of carbon.Nb and
The compound interpolation of V enhances ferrite matrix, reduces the difference of hardness with bainite and martensite phase,
The stretch flangeability of steel plate can be effectively improved.For avoiding excess precipitated phase to reduce ferritic ductility
, the content of Nb of the present invention, V controls 0.010% ~ 0.060% and 0.030% ~ 0.100%, more preferably
0.020% ~ 0.050% and 0.050% ~ 0.080%.
Ca: have and improve ductility and hole expandability by oxide morphology control and raising grain-boundary strength
Effect, be properly added as required.But, too much interpolation steel is mingled with and can increase, instead
And reduce the processing characteristics of steel.The content of Ca of the present invention controls
0.0007% ~ 0.0050%, more preferably 0.0010% ~ 0.0030%.
N: make nitride separate out in steel plate, contributes to strengthening steel plate, but superfluous, then nitride is a large amount of
Separating out, cause elongation percentage, stretch flangeability and spot weldability deterioration, in the present invention, N content controls
Less than 0.005%, more preferably less than 0.0035%.
P, S: for the harmful element in steel.P easily on crystal boundary segregation cause embrittlement, make resistance to impact become
Difference, and unfavorable to spot welding.S is easily formed the field trashes such as MnS in steel, thermally-induced hot-short, and
S is bigger on spot weldability impact.P in the present invention, S content controls respectively 0.015% and 0.010
Below %, more preferably 0.010% and less than 0.008%.
A kind of stretch flangeability and the excellent high strength cold rolled steel plate manufacture method of spot weldability, including smelting
, refine, hot continuous rolling, pickling and cold-rolling, continuous annealing, smooth curling；
After carrying out converter smelting, external refining by said ratio, it is cast into the thick slab of 170 ~ 230mm；
In hot continuous rolling production process, for saving the energy, reducing cost, slab can heat send after continuous casting
Hot charging, carries out hot continuous rolling after heating and thermal insulation.During hot continuous rolling, by heating of plate blank to 1200 ~ 1300 DEG C
, it is incubated 120-180min, prevents the too high burning causing slab of temperature and overheated, and make slab
Tissue and homogenization of composition；Finish rolling start rolling temperature is 1000 ~ 1100 DEG C, and purpose makes finish rolling former
Individual frame realizes recrystallization zone rolling, the rolling load under several frame heavy reductions before reducing；
Finishing temperature is 890 ~ 950 DEG C, and purpose, for alloying element solid solution, separates out with refinement in annealing
Crystal grain, and, in Ar3 high temperature above finish to gauge, beneficially structural homogenity, prevent deformation texture
, anisotropy and the generation of banded structure, improve the stretch flangeability of steel plate；Finishing temperature
No more than 950 DEG C, otherwise recrystallization has excessive abnormal growth to be inclined to, meanwhile, and too high finish to gauge
Temperature causes the growing amount of oxide to be increased dramatically, and pickling (exists the oxidation that deficient pickling does not eliminates
Skin) cold rolling after plate surface quality be deteriorated, reduce stretch flangeability and the spot weldability of steel plate
；Coiling temperature is 650 ~ 700 DEG C, high temperature coiling under this temperature range, at eutectoid reaction subsequently
In easily generate the thicker and carbide of Dispersed precipitate, and the element such as C, Mn is in pearlite
Substantially enrichment, when can reduce annealing austenite in
Critical cooling rate during low temperature phase change, meanwhile, high temperature coiling can make precipitate separate out and long
Greatly, recrystallization temperature is made to reduce, when being conducive to alleviating steel plate annealing, soaking temperature, fast quickly cooling
But the rigors to continuous annealing furnace.Obtaining microscopic structure after hot continuous rolling is ferrite and pearly-lustre
The hot-rolled coil of body, hot-rolled coil thickness is 2.0 ~ 6.5mm；
In pickling and cold-rolling production process, hot-rolled coil is cold rolled to flat cold-rolled sheet after pickling, under cold rolling
Rate is 60 ~ 80%, and cold rolling coil plate thickness is 0.5 ~ 2.5mm, and cold rolling reduction ratio is less than 60%, cold rolling
Efficiency is low, and cold rolling reduction ratio is higher than 80%, and processing hardening is strengthened, and cold roller and deformed drag increases, easily
Cold mill complex load is caused to transfinite.It addition, the pearlite colony spacing in structure of steel under this reduction ratio
Reduce and pearlite is broken more abundant, refine offer condition for the crystal grain in annealing process；
In continuous annealing operation, steel band is 790 ~ 850 DEG C in the soaking zone temperature of annealing furnace, temperature retention time
It is 90 ~ 260s, makes the pearlite in steel be completely reformed into the alloying element such as austenitizing and C, Mn
Spread in austenite from ferrite, improve the stability of austenite.Soaking temperature is less than 79
0 DEG C, the tissue austenitizing degree of steel is inadequate, can not obtain suitable bainite and horse during cooling
Family name's body burden.Soaking temperature is higher than 850 DEG C, and the Ovshinsky scale of construction is many but to dissolve in alloy amount therein relative
Less, the Critical cooling speed of martensite transfor mation and the lower transformation Critical cooling speed of bainite transformation improve,
It is difficult to obtain bainite and martensite under the cooldown rate that annealing furnace is limited.After steel band insulation,
Quickly cooling down two-stage cooling after using first Slow cooling, slow cooling section is cold from holding temperature by steel band
But arriving 670-700 DEG C, cooldown rate is 1 ~ 10 DEG C/s, be for regulation steel in austenite quantity and
Distribution, improves alloying element distributional pattern in austenite and ferrite；Rapid cooling section is with 25 ~ 5
Steel band is cooled to 280 ~ 330 DEG C by the cooldown rate of 0 DEG C/s, is for avoiding perlitic transformation, protects
In card, the bainite and martensite of low temperature changes；After cooling steel band carry out at 280 ~ 330 DEG C out-of-date
Effect processes, and overaging time 350 ~ 950s is air-cooled after timeliness, makes martensite self tempering, coordinates
With ferritic difference of hardness, improve the stretch flangeability of steel plate.
Beneficial effects of the present invention: during smelting by control C element content, add a certain amount of Cr,
Ca element, and compound interpolation Nb, V element, by controlled rolling and controlled cooling during hot rolling
Obtain rational hot rolling microstructure and surface and the excellent hot-rolled substrate of plate shape；Adopt when continuous annealing
By the slow cooling after soaking and twice type of cooling of rapid cooling section, finally give tensile strength at 800MPa
Above, intensity and ductility coupling are good, and stretch flangeability and spot weldability are excellent, thickness 0.5 ~
Between 2.5mm, can be used as the cold-rolled steel sheet of automobile reinforcement and structural member etc..
Accompanying drawing explanation
Fig. 1 is the hot rolled plate microscopic structure of embodiment 1.
Fig. 2 is the cold rolled annealed plate microscopic structure of embodiment 1.
Fig. 3 is the transmission electron microscope photo of the cold rolled annealed plate of embodiment 1.
Fig. 4 is the transmission electron microscope photo of the cold rolled annealed plate of embodiment 1.
The tensile stress-strain curve of the cold rolled annealed plate of Fig. 5.
Detailed description of the invention
By embodiment, the present invention is further described.
The composition of embodiment steel is shown in Table 1, and hot-rolled process parameter is shown in Table 2, and continuous annealing process parameter is shown in Table
3, mechanical property and the characteristic of continuous annealing steel plate are shown in Table 4.
Chemical composition (mass percent) % of table 1 embodiment steel
The rolling technological parameter of table 2 embodiment steel
The continuous annealing process parameter of table 3 embodiment steel
The mechanical property of table 4 embodiment steel annealed sheet and characteristic
By the chemical composition of present invention design, the steel of embodiment is through smelting continuous casting, according to the hot rolling set
Technique controlled rolling and controlled cooling, obtaining thickness is 2.0 ~ 6.5mm, and plate shape and surface quality are good
Hot rolled plate, hot rolled plate tissue is made up of ferrite and pearlite, such as Fig. 1.Hot rolled plate is cold through pickling
Roll into the substrate of 0.5 ~ 2.5mm, then anneal in continuous annealing, the steel plate finally given
Being made up of with a small amount of bainite ferrite and tempered martensite, after annealing, tissue is shown in Fig. 2,3,4,
Its tensile strength is reached for more than 800MPa, Rm× λ >=4500MPa %, intensity and ductility
Coupling is good, and stretch flangeability and spot weldability are excellent.
Claims (2)
1. stretch flangeability and the excellent high strength cold rolled steel plate manufacture method of spot weldability, it is special
Levy and be that described steel plate chemical component weight percentage ratio is: C:0.03%～0.15%, Si:
0.30～0.82%, Mn:1.20%～2.20%, P :≤0.015%, S :≤0.010%,
Al:0.02%～0.15%, N :≤0.005%, Cr:0.20%～0.60%, Nb:
0.010%～0.060%, V:0.030%～0.100%, Ca:0.0007%～0.0050%,
And meeting 1.6%≤Mn+2Nb+V≤2.3%, surplus is that Fe can not with some other
The impurity avoided；Described manufacture method include smelting, refine, hot continuous rolling, pickling and cold-rolling,
Continuous annealing, smooth curling, after carrying out converter smelting, external refining by said ratio,
It is cast into 170～230mm thick slabs；Hot continuous rolling: by heating of plate blank to 1200～1300
DEG C, it being incubated 120-180min, finish rolling start rolling temperature is 1000～1100 DEG C, finishing temperature
Being 890～950 DEG C, coiling temperature 650～700 DEG C, obtaining microscopic structure is ferrite and pearl
The hot-rolled coil of body of light, hot-rolled coil thickness is 2.0～6.5mm；Pickling and cold-rolling: hot rolling
Roll bending is cold rolled to flat cold-rolled sheet after pickling, and cold rolling reduction ratio is 60～80%, cold rolling roll bending
Thickness is 0.5～2.5mm；Continuous annealing: steel band in the soaking zone temperature of annealing furnace is
790～850 DEG C, temperature retention time is 90～260s；After steel band insulation, use first Slow cooling
The most quickly cooling down two-stage cooling, steel band is cooled to 670-700 from holding temperature by slow cooling section
DEG C, cooldown rate is 1～10 DEG C/s；Rapid cooling section with the cooldown rate of 25～50 DEG C/s by steel
Band is cooled to 280～330 DEG C；After annealing, steel band is carried out at overaging at 280～330 DEG C
Reason, the overaging time 350～950s, air-cooled after timeliness.
Stretch flangeability and the excellent high strength cold rolled steel plate of spot weldability the most according to claim 1
Manufacture method, it is characterised in that described high strength cold rolled steel plate chemical component weight percentage ratio is:
C:0.06%～0.11%, Si:0.50～0.70%, Mn:1.60%～2.00%, P :≤
0.010%, S :≤0.008%, Al:0.050%～0.100%, N :≤0.0035%,
Cr:0.30～0.50%, Nb:0.020～0.050%, V:0.050～0.080%, Ca:
0.0010～0.0030%, and meet 1.8%≤Mn+2Nb+V≤2.1%, surplus is Fe
With some other inevitable impurity.
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| MX2017009199A (en) * | 2015-01-16 | 2017-12-07 | Jfe Steel Corp | High-strength steel sheet and production method therefor. |
| MX2018001082A (en) * | 2015-07-27 | 2018-06-06 | Jfe Steel Corp | High strength hot rolled steel sheet and manufacturing method for same. |
| CN105039856A (en) * | 2015-09-11 | 2015-11-11 | 首钢总公司 | High-strength cold-formed automobile axle housing steel and production method thereof |
| KR101736611B1 (en) * | 2015-12-04 | 2017-05-17 | 주식회사 포스코 | Steel having superior brittle crack arrestability and resistance brittle crack initiation of welding point and method for manufacturing the steel |
| EP3705592A4 (en) * | 2018-01-31 | 2020-12-23 | JFE Steel Corporation | High-strength cold-rolled steel sheet, high-strength plated steel sheet, and production methods therefor |
| CN109023149B (en) * | 2018-06-26 | 2020-09-04 | 武汉钢铁有限公司 | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof |
| JP6835294B2 (en) * | 2019-03-07 | 2021-02-24 | 日本製鉄株式会社 | Hot-rolled steel sheet and its manufacturing method |
| CN110257702B (en) * | 2019-06-24 | 2021-04-27 | 鞍钢股份有限公司 | Steel for hot stamping forming and hot forming method thereof |
| CN110724877B (en) * | 2019-10-30 | 2021-05-28 | 鞍钢股份有限公司 | 1180MPa grade high-plasticity bainite complex phase steel plate for automobile and preparation method thereof |
| CN111187985A (en) * | 2020-02-17 | 2020-05-22 | 本钢板材股份有限公司 | Hot-rolled extending flange steel with high hole expansion performance and fatigue life and preparation process thereof |
| CN113403545B (en) * | 2021-05-21 | 2022-07-22 | 鞍钢股份有限公司 | High-hole-expansibility DH1180MPa cold-rolled continuous-annealing steel plate and preparation method thereof |
| CN113528932A (en) * | 2021-05-31 | 2021-10-22 | 唐山钢铁集团高强汽车板有限公司 | Martensite steel plate and preparation method thereof |
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| JP4306497B2 (en) * | 2004-03-10 | 2009-08-05 | Ｊｆｅスチール株式会社 | High-strength cold-rolled steel sheet with excellent workability and post-coating corrosion resistance and method for producing the same |
| JP5088021B2 (en) * | 2007-07-05 | 2012-12-05 | 新日本製鐵株式会社 | High-rigidity, high-strength cold-rolled steel sheet and manufacturing method thereof |
| JP5187320B2 (en) * | 2010-01-06 | 2013-04-24 | 新日鐵住金株式会社 | Cold rolled steel sheet manufacturing method |
| JP5477002B2 (en) * | 2010-01-13 | 2014-04-23 | 新日鐵住金株式会社 | Cold rolled steel sheet |
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