CN108531832A - 800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof - Google Patents
800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof Download PDFInfo
- Publication number
- CN108531832A CN108531832A CN201810293172.0A CN201810293172A CN108531832A CN 108531832 A CN108531832 A CN 108531832A CN 201810293172 A CN201810293172 A CN 201810293172A CN 108531832 A CN108531832 A CN 108531832A
- Authority
- CN
- China
- Prior art keywords
- cold
- yield
- rolling
- steel
- ratio
- 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
- 239000010960 cold rolled steel Substances 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title description 17
- 229910052802 copper Inorganic materials 0.000 claims abstract description 11
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 10
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 90
- 239000010959 steel Substances 0.000 claims description 90
- 238000001816 cooling Methods 0.000 claims description 28
- 238000000137 annealing Methods 0.000 claims description 25
- 238000005097 cold rolling Methods 0.000 claims description 23
- 229910000859 α-Fe Inorganic materials 0.000 claims description 18
- 238000002791 soaking Methods 0.000 claims description 15
- 238000000034 method Methods 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 14
- 229910001562 pearlite Inorganic materials 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 7
- 239000004615 ingredient Substances 0.000 claims description 7
- 238000005554 pickling Methods 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 7
- 238000010583 slow cooling Methods 0.000 claims description 7
- 238000004321 preservation Methods 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- 239000010949 copper Substances 0.000 description 22
- 229910001566 austenite Inorganic materials 0.000 description 11
- 239000010955 niobium Substances 0.000 description 11
- 229910001563 bainite Inorganic materials 0.000 description 10
- 239000010936 titanium Substances 0.000 description 10
- 230000008569 process Effects 0.000 description 9
- 238000001556 precipitation Methods 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- 230000009466 transformation Effects 0.000 description 6
- 229910001275 Niobium-titanium Inorganic materials 0.000 description 5
- 238000005275 alloying Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000005516 engineering process Methods 0.000 description 5
- RJSRQTFBFAJJIL-UHFFFAOYSA-N niobium titanium Chemical compound [Ti].[Nb] RJSRQTFBFAJJIL-UHFFFAOYSA-N 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 230000001376 precipitating effect Effects 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 230000003014 reinforcing effect Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000008859 change Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 230000009931 harmful effect Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 239000013049 sediment Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 241001417490 Sillaginidae Species 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- CKUAXEQHGKSLHN-UHFFFAOYSA-N [C].[N] Chemical compound [C].[N] CKUAXEQHGKSLHN-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 150000007513 acids Chemical class 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 150000001721 carbon Chemical group 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000035568 catharsis Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000006698 induction 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
- 208000020442 loss of weight Diseases 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- -1 meanwhile Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000005192 partition Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000002910 structure generation Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—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
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/009—Pearlite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses an 800 MPa-grade high-yield-ratio cold-rolled steel plate, which comprises the following components in percentage by weight: 0.05-0.12%, Si: 0.10 to 0.50%, Mn: 1.20% -1.80%, P: less than or equal to 0.015%, S: less than or equal to 0.010 percent, Al: 0.02% -0.10%, N: less than or equal to 0.005%, Sb: 0.015 to 0.050%, Nb: 0.020 to 0.050%, Ti: 0.050-0.100%, and the contents of Nb, Ti and Cr are more than or equal to 0.070% and less than or equal to 0.150%: 0.050 to 0.100%, Cu: 0.10 to 0.60%, Ni: 0.050-0.100%, and the balance of Fe and other inevitable impurities.
Description
Technical field
The invention belongs to automobile cold-rolled high intensity thin slab technique fields, provide a kind of 800MPa grades of high-yield-ratio cold rolling
Steel plate and its manufacturing method.
Background technology
Modern and future automobile development trend is low energy consumption, loss of weight and high safety, for this hair of adaptation auto industry
Automaker is just being actively working to body of a motor car " lightweight " product in one's power for exhibition trend, steel production enterprise and Research Center
Research and development, the design of body of a motor car and high-strength steel parts.The high strength steel developed at present such as two-phase (DP) steel, phase change induction modeling
The automobile cold-rolled high strength steels such as property (TRIP) steel, twinning induced plasticity (TWIP) steel and quenching partition (Q＆P) steel have industrialized
Volume production, the parts such as frame member, door anti-collision joist, bumper and seat slide for automobile.Realize Automobile
Body " lightweight " requirement.Since the automobile structure forming manufactured with these high strength steel plates is relatively easy, the deflection of steel plate is not
Greatly, work-hardening capacity is not high, although the yield strength of baking vanish process light plate after forming increases, meets vehicle body
Strength and stiffness.But these advanced cold rolling high strength steels are produced, the cooling section to continuous annealing furnace and aging section ability
More demanding, annealing process control is harsh, and production difficulty is high.To reduce cold rolling high strength steel production difficulty, and ensure with high-strength
Spend steel plate manufacture vehicle body have enough strength and stiffness, meet body of a motor car " lightweight ", need cold-rolled steel sheet at
Micro alloying element is added in point, and production technology is improved, and cold-rolled steel sheet is made to have both high yield tensile ratio and excellent modeling
Property.
CN101376944A is related to a kind of high-strength high-tensile ratio cold-rolled steel sheet and its manufacturing method, the surrender of steel plate are strong
Degree is more than 500MPa, and tensile strength is more than 600MPa, and yield tensile ratio is more than 0.80.It is more than 600MPa, Qu Qiang to obtain this intensity
Than the steel plate more than 0.80, in annealing process, steel plate is heated to being cooled fast to by two-part after 780-850 DEG C of heat preservation
200 DEG C hereinafter, this technique first segment is easy to control from high temperature rapid cooling, and second segment under 400-500 DEG C of lower temperature quickly
Be cooled to 200 DEG C hereinafter, to by gas cooling mode continuous annealing line production for it is difficult, do not have practical behaviour
The property made.
CN101558178A provides a kind of cold-rolled steel sheet with high-yield-ratio and excellent weather resistance, adds in the steel grades
Nb, Ni are entered, the alloying elements such as Co, Cr, Cu and B are by the steel plate after cold rolling at 500 DEG C to A1The temperature range of transition point
Interior continuous annealing, the yield tensile ratio for obtaining steel plate are more than 0.85, and tensile strength is more than 800MPa, is mainly used for building, rail traffic
Tool and Production Container, it is more not comparable than the product of cold rolling high strength steel plate and continuous annealing process with automobile high yield
Property.
CN102492823A provides a kind of continuous annealing process of yield strength 420MPa grades of cold rolling low alloy high strength steel plates,
By the way that the cold rolling low alloy high strength steel plate containing Ti, Nb chemical element is heated to 800 ± 10 DEG C of heat preservations, then slow cooling through two sections
It is quickly cooled down to 600 ± 20 DEG C, cooling end temp is 270 ± 20 DEG C, is finally such as water-cooled to room temperature, obtains yield strength about
For 430MPa, tensile strength is about 500MPa, the steel plate that elongation after fracture is about 21%.This technique is by continuous annealing furnace rapid cooling
Section is identical with the adjustment of the cooling rate of overaging section, reduces the cooling time of steel plate.But this annealing process is to continuous annealing
The cooling rate requirement of stove overaging section is excessively high, and it is too big to be quickly cooled down difficulty in low temperature realization.Therefore, annealed wire overaging section
It is unrealistic to be quickly cooled down technique.
Invention content
For the defect of currently available technology, present invention aims at smelt having on ingredient and production technology by steel clock
Effect control realizes that the fetrite grain refinement of steel plate, the complex intensifying effect of precipitation strength and phase transformation strengthening can connect in industry
Yield strength is produced on continuous annealed wire in 800MPa or more, elongation after fracture is more than 12.0%, and yield tensile ratio is more than 0.85 height
Yield tensile ratio, and the cold-rolled steel sheet and its manufacturing method of plasticity and cold forming function admirable, manufactured steel plate can be used as automobile
Structural member, such as the frame member of automobile, door anti-collision joist, bumper and seat slide parts.
Purpose of the present invention is to what is realized by following technical solution：
A kind of 800MPa grades of high-yield-ratio cold-rolled steel sheet, it is characterised in that ingredient is by weight percent：C：0.05%~
0.12%, Si：0.10~0.50%, Mn：1.20%~1.80%, P：≤ 0.015%, S：≤ 0.010%, Al：0.02%~
0.10%, N：≤ 0.005%, Sb：0.015~0.050%, Nb：0.020~0.050%, Ti：0.050~0.100%, and
Meet 0.070%≤Nb+Ti≤0.150%, Cr：0.050~0.100%, Cu：0.10~0.60%, Ni：0.050~
0.100%, surplus is Fe and some other inevitable impurity.
A kind of 800MPa grades of high-yield-ratio cold-rolled steel sheet, it is characterised in that ingredient is by weight percent：C：0.07%~
0.10%, Si：0.25~0.35%, Mn：1.45%~1.65%, P：≤ 0.010%, S：≤ 0.005%, Al：0.05%~
0.08%, N：≤ 0.003%, Sb：0.025~0.040%, Nb：0.030~0.040%, Ti：0.060~0.090%, and
Meet 0.090%≤Nb+Ti≤0.130%, Cr：0.060~0.090%, Cu：0.30~0.50%, Ni：0.070~
0.090%, surplus is Fe and some other inevitable impurity.
The yield tensile ratio of the 800MPa grade high-yield-ratio cold-rolled steel sheets is more than 0.85.
A kind of 800MPa grades of high-yield-ratio cold-rolled steel sheet manufacturing method, including converter smelting, external refining, casting, hot rolling,
Pickling and cold-rolling and continuous annealing, it is characterised in that：The hot rolling is slab hot delivery and hot charging, and hot continuous rolling is carried out after heating and thermal insulation,
When hot continuous rolling, by heating of plate blank to 1150~1250 DEG C, 120-150min is kept the temperature, finish rolling start rolling temperature is 1000~1100 DEG C,
Finishing temperature is 860~920 DEG C, 580~630 DEG C of coiling temperature, obtains the hot rolled coil that microscopic structure is ferrite and pearlite
Plate, hot-rolled coil thickness are 2.0~6.0mm；The pickling and cold-rolling is that cold rolling reduction ratio is 60~80%, cold rolling coil plate thickness
For 0.5~2.0mm；Described in continuous annealing be steel band in the soaking zone temperature of annealing furnace is 720~770 DEG C, soaking heat preservation
Time is 100~250s；After steel band heat preservation, using being quickly cooled down two-stage cooling after first Slow cooling；Slow cooling section by steel band from
Holding temperature is cooled to 580-650 DEG C, and cooling rate is 1~5 DEG C/s；Rapid cooling section is with the cooling rate of 10~15 DEG C/s by steel band
400~460 DEG C are cooled to, then carries out Wetted constructures at 400~460 DEG C, 450~900s of overaging time, after timeliness
It is air-cooled, smooth to batch.
Steel grades control principle of the present invention is as follows：
C：Intensified element basic in steel, can active balance steel intensity and ductility.And efficiently generate bainite
Element, for ensure steel high-yield-ratio, the present invention in C control 0.05%~0.12%, more preferable 0.07%~0.10%.
Si：It is ferrite generating elements, promotes carbon to austenite segregation and inhibit the formation of carbide, to solid in ferrite
Molten carbon has removing and catharsis, to avoid gap solution strengthening.The present invention relies primarily on the carbonitride of niobium titanium in ferrite
Precipitation strength and crystal grain refinement in phase improve ferrite intensity, have high yield strength to reach steel plate.Therefore, originally
Si controls are 0.10~0.50%, more preferable 0.25~0.35% in invention.
Mn：Belonging to and expands austenite phase field, the element of stable austenite can effectively improve the quenching degree on austenite island,
Remaining austenite is transformed into cooling rate necessary to martensite after steel plate middle temperature transformation thus can be reduced, and plays solid solution
Strengthen the effect with fining ferrite grains.High Mn content easily causes band-like group based on cementite, pearlite and bainite
It knits, and influences the welding performance of steel plate.Mn contents of the present invention control 1.20%~1.80%, more preferable 1.45%~
1.65%.
Al：Al is main deoxidier, while Al can also form AlN precipitations, play certain Grain refinement.Steel
When middle Al is added for deoxidation, unsuitable too low, otherwise Mn, Si etc. coarse oxide largely disperses in steel, deteriorates steel,
But excessive tufted aluminium oxide inclusion increases, and so that the plasticity of steel and weldability is deteriorated, and can influence steel-making and continuous casting, this
Al content control is 0.02%~0.10%, more preferable 0.05%~0.08% in invention.
Sb：It is a kind of low melting point element, molten steel flow can be improved, hinder carbon atom diffusion, hence it is evident that promotes and stablize pearl
Body of light is formed, and improves matrix hardness, while steel matrix can be inhibited to be corroded, and enrichments of the Sb on MnS field trashes is precipitated, energy
The formation for promoting Intragranular Acicular Ferrite in steel is conducive to the plasticity for improving steel.Sb contents of the present invention control 0.015~0.050%,
More preferable 0.025~0.040%%.
Nb, Ti：It is the element for the yield strength and crystal grain thinning for effectively improving steel with precipitation strength effect.Add in steel
Enter Nb and Ti elements, forms carbonitride, refining grain size and the effect for keeping carbon.So that ferrite matrix is strengthened, drops
The difference of hardness of low ferrite and pearlite and bainite phase effectively improves the yield strength and cold formability energy of steel plate.It is thin to make
Change ferrite grain size and improve ferritic intensity, the content of Nb of the present invention, Ti are controlled in 0.020~0.050% He
0.050~0.100%, more preferable 0.030~0.040% and 0.060~0.090%, and 0.090%≤Nb+Ti of satisfaction≤
0.130%.
Cr：Middle carbide significantly improves intensity, hardness and wearability, can improve steel inoxidizability and
Corrosion resistance makes A3And A1Temperature increases, and GS lines are moved to upper left side.The content control of Cr of the present invention 0.050~0.100%,
More preferable 0.060~0.090%.
Cu：Steel intensified element and the corrosion resistance element for improving steel, meanwhile, Cu can improve the stability of austenite, favorably
In the formation of bainite.The precipitate of Cu can improve the intensity and hardness of steel, and Cu precipitated phases have good plasticity, without
The high stress concentration zone or crackle easily generated near Cu precipitated phases is conducive to the service life for improving steel plate.In addition, Cu can be carried
The corrosion resistance of Gao Gang simultaneously can eliminate harmful effects of the S to corrosion resistance.In the present invention control of Cu contents 0.10~
0.60%, more preferable 0.30~0.50%.
Ni：It is the effective element of austenitizing, can prevents to add fracture of the Cu steel in casting process.The critical of steel can be reduced
Cooling velocity improves the quenching degree and intensity of steel, without reducing its plasticity, improves the low-temperature flexibility and fatigue resistance of steel.In addition,
Ni has certain corrosion resistance, has good anti-corrosion capability to some reproducibility acids.In the present invention control of Ni contents 0.050~
0.100%, more preferable 0.070~0.090%.
N：So that nitride is precipitated in steel plate, helps to strengthen steel plate, but superfluous, then nitride is largely precipitated, and causes to prolong
Stretch rate, weldability deterioration and steel plate cold forming degradation, the present invention in N content control 0.005% hereinafter, more preferably
0.003% or less.
P, S：For the harmful element in steel.P segregations easily on crystal boundary cause embrittlement, S easily to form MnS etc. in steel and be mingled with
Object makes the toughness plasticity of steel be deteriorated.P in the present invention, S content are controlled respectively in 0.015% and 0.010% hereinafter, more preferably
0.010% and 0.005% or less.
The present invention selects the reason of technological parameter in above-mentioned each feature as follows：
Slab soaking temperature is between 1150~1250 DEG C, soaking time 120-150min.Soaking temperature control exists
1150 DEG C or more, to increase the solid solution capacity of Nb, precipitating reinforcing effect is improved, but soaking temperature is not above 1250 DEG C, to avoid
Slab overheat and burning and Cu high temperature caused by crystal boundary segregation are hot-short.Soaking time controls between 120-150min, is
Make the tissue and ingredient full and uniformization of slab, and avoids the energy consumption of heating time long generation.
Finish rolling start rolling temperature controls between 1000~1100 DEG C, is in order to which several racks realize recrystallization zone before finish rolling
Rolling, the mill milling load before reducing under several rack heavy reductions.
Finishing temperature control between 860~920 DEG C, is precipitated in annealing to refine crystalline substance in order to which alloying element is dissolved
Grain.Also, in Ar3 or more high-temperature final rollings, is conducive to structural homogenity, prevents deformation texture, anisotropy and banded structure
Generation.Finishing temperature is no more than 920 DEG C, to prevent the excessive abnormal growth of recrystal grain and copper to be precipitated.Meanwhile it is excessively high
Finishing temperature causes the production quantity of oxide increased dramatically, and the plate surface quality after pickling and cold-rolling is deteriorated, and reduces the modeling of steel plate
Property.
Oiler temperature control batches between 580~630 DEG C under this temperature range, can effectively refine pearlite, also may be used
To prevent the Carbonitride Precipitation object of niobium titanium to be roughened, ferrite crystal grain is prevented to grow up.Meanwhile being conducive to the precipitation of Cu precipitates, it rises
To precipitating reinforcing effect.
The control of cold rolling reduction ratio is to give full play to cold rolling mill energy between 60~80% after pickling after hot-rolled coil
Power.Cold rolling reduction ratio is less than 60%, and cold rolling efficiency is low, and cold rolling reduction ratio is higher than 80%, and processing hardening is reinforced, cold-rolling deformation drag
Increase, easily causing cold mill complex load transfinites.In addition, the pearlite colony spacing under this reduction ratio in structure of steel reduces and pearlite
It is broken more abundant, condition is provided for the crystal grain refinement in annealing process.
Soaking temperature should control between 720~770 DEG C when continuous annealing, and soaking time is 100~250s.To make in steel
Part perlitic transformation be the alloying elements such as austenite and C, Mn from being spread into austenite in ferrite, improve austenite
Stability.Soaking temperature is less than 720 DEG C, and the tissue of steel fails austenitizing, and a certain amount of bainite cannot be obtained when cooling.
Hot temperature is higher than 770 DEG C, and Ovshinsky scale of construction increases but dissolves in that alloy amount therein is relatively fewer, and the lower transformation of bainite transformation is critical
Cooling rate improves, and steel band is not easy to obtain bainite when cooling down, while weakening Cu precipitating reinforcing effects because the precipitate of Cu is roughened, and makes
The yield strength of steel reduces.
Steel band is cooled to 580~650 DEG C from soaking temperature in continuous annealing line slow cooling section, cooling rate is 1~5 DEG C/
S is to improve distributional pattern of the alloying element in austenite and ferrite to adjust the quantity of austenite and distribution in steel.Soon
Steel plate is cooled to 400~460 DEG C by the cold section of cooling rate with 10~15 DEG C/s, is the low-temperature transformation product to generate a small amount of
The sediment of bainite and Cu, 450~900s of overaging after steel plate rapid cooling, makes Cu sediments further be precipitated, and improves bending for steel
Intensity, while tunable bainite and ferritic difference of hardness are taken, the plasticity of steel plate is improved.
The beneficial effects of the invention are as follows：By controlling the content of C, Mn and Si element, and compound addition when the present invention smelts
The elements such as a certain amount of Nb and Ti elements and Sb, Cr and Cu, controlled rolling and controlled cooling when passing through hot rolling obtain rational hot rolling microstructure
The excellent hot-rolled substrate with surface and plate shape；In continuous annealing using after soaking slow cooling and the rapid cooling section type of cooling twice,
It finally obtains yield strength and is more than 800MPa, tensile strength is more than 12.0% in 860MPa or more, elongation after fracture, and yield tensile ratio is big
In 0.85, the cold-reduced sheet of high-yield-ratio and plasticity and cold forming function admirable of the thickness between 0.5~2.0mm, manufacture it is cold
It rolls plate and can be used as automobile reinforcer and structural member, meet requirement of the body of a motor car to strength and stiffness.
Description of the drawings
Fig. 1 is cold rolled annealed plate microscopic structure of the present invention；
Fig. 2 is the carbonitride of niobium titanium in annealed sheet tissue；
Fig. 3 is the precipitate of copper in annealed sheet tissue；
Specific implementation mode
It is illustrated with reference to specific embodiment：
The ingredient 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, continuous annealing
The mechanical property of steel plate is shown in Table 4.The microscopic structure of the cold rolled annealed plate of embodiment is shown in Fig. 1, the carbon nitrogen of niobium titanium in annealed sheet tissue
Compound is shown in Fig. 2, and the precipitate of copper is shown in Fig. 3 in annealed sheet tissue.
Chemical composition (mass fraction) % of 1 embodiment steel of table
The rolling technological parameter of 2 embodiment steel of table
The continuous annealing process parameter of 3 embodiment steel of table
The mechanical property of 4 embodiment steel annealed sheet of table
By the chemical composition that designs of the present invention, the steel of embodiment is through smelting continuous casting, slab thickness 170-230mm, according to
The hot rolling technology controlled rolling and controlled cooling of setting, it is 2.0~6.0mm, plate shape and the good hot rolled plate of surface quality, hot rolled plate to obtain thickness
Tissue is made of ferrite and pearlite, and ferrite grain size is tiny.Hot rolled plate is through pickling and cold-rolling at the base of 0.5~2.0mm
Then plate is annealed on continuous annealing line, finally obtained steel plate tissue is by ferrite, pearlite and a small amount of bainite group
At, and have the precipitate of the Carbonitride Precipitation object and copper of the niobium titanium of a large amount of small and dispersed distributions, play reinforced ferrite work
With improving the yield strength of cold rolled annealed steel plate.The cold-rolled steel sheet yield strength prepared is more than 800MPa, and tensile strength exists
860MPa or more, elongation after fracture are more than 12.0%, yield tensile ratio Rp0.2/Rm>=0.85, yield strength is high and plasticity and cold formability
It can be excellent.
Claims (4)
1. a kind of 800MPa grades of high-yield-ratio cold-rolled steel sheet, it is characterised in that ingredient is by weight percent：C：0.05%~
0.12%, Si：0.10~0.50%, Mn：1.20%~1.80%, P：≤ 0.015%, S：≤ 0.010%, Al：0.02%~
0.10%, N：≤ 0.005%, Sb：0.015~0.050%, Nb：0.020~0.050%, Ti：0.050~0.100%, and
Meet 0.070%≤Nb+Ti≤0.150%, Cr：0.050~0.100%, Cu：0.10~0.60%, Ni：0.050~
0.100%, surplus is Fe and some other inevitable impurity.
2. 800MPa grades of high-yield-ratio cold-rolled steel sheet according to claim 1, it is characterised in that ingredient is by weight percent
For：C：0.07%~0.10%, Si：0.25~0.35%, Mn：1.45%~1.65%, P：≤ 0.010%, S：≤
0.005%, Al：0.05%~0.08%, N：≤ 0.003%, Sb：0.025~0.040%, Nb：0.030~0.040%, Ti：
0.060~0.090%, and meet 0.090%≤Nb+Ti≤0.130%, Cr：0.060~0.090%, Cu：0.30~
0.50%, Ni：0.070~0.090%, surplus is Fe and some other inevitable impurity.
3. 800MPa grades of high-yield-ratio cold-rolled steel sheet according to claim 1, it is characterised in that the 800MPa grades are high
The yield tensile ratio of tensile ratio cold-rolled steel sheet is more than 0.85.
4. a kind of manufacturer of the 800MPa grade high-yield-ratio cold-rolled steel sheets described in claim 1-3 any one claims
Method, including converter smelting, external refining, casting, hot rolling, pickling and cold-rolling and continuous annealing, it is characterised in that：The hot rolling will
Heating of plate blank keeps the temperature 120-150min to 1150~1250 DEG C, and finish rolling start rolling temperature is 1000~1100 DEG C, and finishing temperature is
860~920 DEG C, 580~630 DEG C of coiling temperature obtains the hot-rolled coil that microscopic structure is ferrite and pearlite, hot-rolled coil
Thickness is 2.0~6.0mm；The pickling and cold-rolling is that cold rolling reduction ratio is 60~80%, cold rolling coil plate thickness be 0.5~
2.0mm；Described in continuous annealing be steel band in the soaking zone temperature of annealing furnace is 720~770 DEG C, and soaking soaking time is
100~250s；After steel band heat preservation, using being quickly cooled down two-stage cooling after first Slow cooling；Slow cooling section is warm from heat preservation by steel band
Degree is cooled to 580-650 DEG C, and cooling rate is 1~5 DEG C/s；Steel band is cooled to by rapid cooling section with the cooling rate of 10~15 DEG C/s
400~460 DEG C, then carry out Wetted constructures at 400~460 DEG C, 450~900s of overaging time is air-cooled, flat after timeliness
Entire volume takes.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810293172.0A CN108531832A (en) | 2018-03-30 | 2018-03-30 | 800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810293172.0A CN108531832A (en) | 2018-03-30 | 2018-03-30 | 800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN108531832A true CN108531832A (en) | 2018-09-14 |
Family
ID=63483073
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810293172.0A Pending CN108531832A (en) | 2018-03-30 | 2018-03-30 | 800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108531832A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109440015A (en) * | 2018-11-12 | 2019-03-08 | 包头钢铁（集团）有限责任公司 | A kind of 400MPa grades of cold rolling sliding rail steel and its manufacturing method |
| CN109694997A (en) * | 2019-02-25 | 2019-04-30 | 上海大学 | Change the heat treatment process for promoting Fe-Mn-Al-C Mechanical Properties of Dual Phase Steels using γ → α ppolymorphism |
| CN111088463A (en) * | 2020-01-21 | 2020-05-01 | 鞍钢股份有限公司 | Steel bar resistant to corrosion in low-temperature atmospheric environment and production method thereof |
| CN115404408A (en) * | 2022-08-30 | 2022-11-29 | 鞍钢股份有限公司 | High-yield-ratio cold-rolled steel plate with excellent forming performance and manufacturing method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008156680A (en) * | 2006-12-21 | 2008-07-10 | Nippon Steel Corp | High-strength cold rolled steel sheet having high yield ratio, and its production method |
| JP2012082499A (en) * | 2010-10-14 | 2012-04-26 | Sumitomo Metal Ind Ltd | Hot-dipped steel sheet and method for producing the same |
| CN104745942A (en) * | 2013-12-25 | 2015-07-01 | Posco公司 | Cold rolled steel sheet having high yield ratio and excelent impact property and method for manufacturing the same |
| CN106164313A (en) * | 2014-03-31 | 2016-11-23 | 杰富意钢铁株式会社 | High yield ratio and high-strength cold-rolled steel sheet and manufacture method thereof |
| CN107164700A (en) * | 2017-05-27 | 2017-09-15 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacture method |
| CN107217209A (en) * | 2016-03-22 | 2017-09-29 | 株式会社Posco | Delamination resistance and the excellent high-yield-ratio type cold-rolled steel sheet of collision characteristic and its manufacture method |
-
2018
- 2018-03-30 CN CN201810293172.0A patent/CN108531832A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008156680A (en) * | 2006-12-21 | 2008-07-10 | Nippon Steel Corp | High-strength cold rolled steel sheet having high yield ratio, and its production method |
| JP2012082499A (en) * | 2010-10-14 | 2012-04-26 | Sumitomo Metal Ind Ltd | Hot-dipped steel sheet and method for producing the same |
| CN104745942A (en) * | 2013-12-25 | 2015-07-01 | Posco公司 | Cold rolled steel sheet having high yield ratio and excelent impact property and method for manufacturing the same |
| CN106164313A (en) * | 2014-03-31 | 2016-11-23 | 杰富意钢铁株式会社 | High yield ratio and high-strength cold-rolled steel sheet and manufacture method thereof |
| CN107217209A (en) * | 2016-03-22 | 2017-09-29 | 株式会社Posco | Delamination resistance and the excellent high-yield-ratio type cold-rolled steel sheet of collision characteristic and its manufacture method |
| CN107164700A (en) * | 2017-05-27 | 2017-09-15 | 唐山钢铁集团有限责任公司 | A kind of 800MPa grades of high-yield-ratio cold-rolled strip and its manufacture method |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109440015A (en) * | 2018-11-12 | 2019-03-08 | 包头钢铁（集团）有限责任公司 | A kind of 400MPa grades of cold rolling sliding rail steel and its manufacturing method |
| CN109694997A (en) * | 2019-02-25 | 2019-04-30 | 上海大学 | Change the heat treatment process for promoting Fe-Mn-Al-C Mechanical Properties of Dual Phase Steels using γ → α ppolymorphism |
| CN109694997B (en) * | 2019-02-25 | 2021-08-06 | 上海大学 | Heat treatment process for improving mechanical property of Fe-Mn-Al-C dual-phase steel by utilizing gamma → alpha isomerous transformation |
| CN111088463A (en) * | 2020-01-21 | 2020-05-01 | 鞍钢股份有限公司 | Steel bar resistant to corrosion in low-temperature atmospheric environment and production method thereof |
| CN111088463B (en) * | 2020-01-21 | 2021-04-27 | 鞍钢股份有限公司 | Steel bar resistant to corrosion in low-temperature atmospheric environment and production method thereof |
| CN115404408A (en) * | 2022-08-30 | 2022-11-29 | 鞍钢股份有限公司 | High-yield-ratio cold-rolled steel plate with excellent forming performance and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105274432B (en) | 600 MPa-grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof | |
| CN107177770B (en) | The production method of cold rolling low alloy high strength steel plate | |
| CN109023036B (en) | Ultrahigh-strength hot-rolled complex-phase steel plate and production method thereof | |
| CN102586688B (en) | A kind of dual phase sheet steel and manufacture method thereof | |
| CN106282831B (en) | A kind of high-strength container weather resisting steel and its manufacturing method | |
| CN103882320B (en) | High-strength cold-rolled steel sheet having excellent stretch flangeability and spot weldability, and method for producing same | |
| CN103080357B (en) | High-strength cold-rolled steel sheet having excellent stretch flange properties, and process for production thereof | |
| CN110093552A (en) | A kind of high strength and ductility Q&P steel plate and preparation method thereof that welding performance is excellent | |
| CN109295283A (en) | A kind of method that short annealing prepares 1000MPa grades of high ductile steels | |
| CN107250406B (en) | High strength cold rolled steel plate and its manufacturing method | |
| CN110453146A (en) | A kind of Cr alloying steel of no yield point elongation and preparation method thereof | |
| CN106498278A (en) | Low-density cut deal of a kind of high-strength high-elongation ratio and preparation method thereof | |
| CN105189804B (en) | High-strength steel sheet and its manufacture method | |
| CN103320701B (en) | A kind of ferrite-bainite AHSS plate and manufacture method thereof | |
| CN108707815A (en) | A kind of 800MPa grades of pure zinc coating high-chambering steel plate and its manufacturing method | |
| CN107699791B (en) | 900MPa grades high cold-bending property low alloy high strength steel plate and preparation method thereof | |
| CN101649420A (en) | Ultra-strength, high toughness and low yield ratio steel and steel plate and manufacturing method thereof | |
| CN104513927A (en) | High-strength high-rigidity steel plate with tensile strength of 800 MPa and preparation method thereof | |
| CN103014545B (en) | High-strength steel plate with 900 Mpa-level yield strength and preparation method of steel plate | |
| CN108531832A (en) | 800 MPa-grade high-yield-ratio cold-rolled steel plate and manufacturing method thereof | |
| CN109943765B (en) | 800 MPa-grade cold-rolled dual-phase steel with high yield ratio and preparation method thereof | |
| KR20230166081A (en) | Low-carbon, low-alloy Q&P steel or hot-dip galvanized Q&P steel with a tensile strength of 1180 MPa or more and manufacturing method thereof | |
| CN110129673A (en) | A kind of 800MPa grades of high strength and ductility Q&P steel plate and preparation method thereof | |
| CN109385570B (en) | High-strength steel plate and manufacturing method thereof | |
| CN109898017A (en) | Cold-rolled dual-phase steel with excellent 1000 MPa-level cold bending performance and production method thereof |
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 | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20180914 |
|
| WD01 | Invention patent application deemed withdrawn after publication |