CN106086638B - A kind of Galvanized Dual Phase Steel and its production method - Google Patents
A kind of Galvanized Dual Phase Steel and its production method Download PDFInfo
- Publication number
- CN106086638B CN106086638B CN201610439055.1A CN201610439055A CN106086638B CN 106086638 B CN106086638 B CN 106086638B CN 201610439055 A CN201610439055 A CN 201610439055A CN 106086638 B CN106086638 B CN 106086638B
- Authority
- CN
- China
- Prior art keywords
- dual phase
- phase steel
- temperature
- annealing
- cold
- 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.)
- Active
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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention belongs to cold-rolled steel technical field, a kind of Galvanized Dual Phase Steel and its production method are disclosed.Its component and weight percent content are：C：0.085~0.115%, Si：0.15~0.24%, Mn：1.45~1.55%, P：≤ 0.015%, S：≤ 0.005%, Alt：0.025~0.065%, Cr：0.14~0.24%, Mo：0.24~0.29%, N：≤ 0.006%, remaining is iron and other inevitable impurity.Production method：KR desulfurization process, LF+RH refining treatments, RH Calcium treatments, continuous casting, heating steel billet, roughing, finish rolling, section cooling, is batched at pneumatic steelmaking；Uncoiling, cold continuous rolling, is batched at pickling；Uncoiling, annealing, zinc-plated, finishing, is batched at cleaning.The Galvanized Dual Phase Steel of the present invention is by composition design, technology controlling and process, whether there is or not the annealing producing lines of rapid cooling section to be applicable in.
Description
Technical field
The present invention relates to cold-rolled steel technical field more particularly to a kind of Galvanized Dual Phase Steel and its production methods.
Background technology
Cold-strip steel is mainly used for the industries such as automobile, household electrical appliances, and China's auto output was advanced by leaps and bounds in recent years, was expanded significantly
The market capacity of flat cold-rolled sheet, especially zinc coated sheet are many due to increasingly increasing with good corrosion resisting property dosage
Cold-rolling galvanization thin plate is positioned as the key product of high-quality, high added value by more iron and steel enterprises.In addition, as automobile industry is quick
Development, to reduce automobile energy consumption, the necessary loss of weight of body of a motor car, this requires automobiles more to use high-strength steel.In view of above two
Point, demand of the modern automobile industry to cold-rolling galvanization high-strength steel and require it is higher and higher.
The annealing furnace of the cold-rolling galvanization high-strength steel producing line of steel production enterprise is divided into two kinds by for the type of cooling, when
In soaking zone to strip between zinc-plated first through slow cooling section, a part of ferrite is precipitated, then passes through rapid cooling section, is cooled to zinc-plated temperature soon
460 DEG C or so of degree, generates a small amount of bainite, and this producing line is suitble to the production of traditional cold-rolling galvanization dual phase steel；Second is that in soaking
Section is to only slow cooling section undergoes longer slow cooling section without rapid cooling section, i.e. strip from high temperature between zinc-plated, and direct slow cooling is to 460 DEG C
(zinc pot temperature) is zinc-plated into zinc pot, and this producing line is generally adapted the production of galvanized mild steel.
Since the type of cooling of zinc-plated producing line annealing unit is different, it is suitble to the strip type produced also different from, it is right
It in this kind of high-strength steel of two-phase (DP) steel, generally requires from high temperature and is cooled to middle warm area soon, shorten the time in middle warm area as possible to keep away
Exempt from middle warm area and forms a large amount of bainite structure.For iron and steel enterprise, when cold-rolling galvanization dual phase steel production task increases,
All producing lines cannot can only be made full use of, so as to cause production efficiency and production capacity in the producing line production of its adaptation
It reduces.Prouctiveness is the important goal that enterprise is pursued, therefore is developed a kind of not by the zinc-plated cold rolling that the type of cooling is influenced before
Galvanized Dual Phase Steel is significant to the economic benefit of iron and steel enterprise, prouctiveness.
Invention content
Technical problem to be solved by the invention is to provide a kind of not by the zinc-plated cold-rolling galvanization that the type of cooling is influenced before
Dual phase steel and its production method.
In order to solve the above technical problems, according to an aspect of the invention, there is provided a kind of Galvanized Dual Phase Steel, component and
Weight percent content is：C：0.085~0.115%, Si：0.15~0.24%, Mn：1.45~1.55%, P：≤
0.015%, S：≤ 0.005%, Alt：0.025~0.065%, Cr：0.14~0.24%, Mo：0.24~0.29%, N：≤
0.006%, remaining is iron and other inevitable impurity.
Preferably, the yield strength of the Galvanized Dual Phase Steel is 350~425MPa, and tensile strength is 600~670MPa.
Preferably, the elongation after fracture A of the Galvanized Dual Phase Steel80For 22~27%, n10-20Value is 0.16~0.18.
Preferably, the width of the Galvanized Dual Phase Steel is 1000~1860mm, and thickness is 0.3~2.5mm.
According to another aspect of the present invention, a kind of method producing above-mentioned Galvanized Dual Phase Steel is provided, including：
Molten iron is obtained into strand by KR desulfurization pretreatments, converter smelting, LF+RH refining treatments, RH Calcium treatments, continuous casting；
The strand is heated；By fixed width pressure, required strand width is obtained；It is obtained by roughing, finish rolling
Obtain hot rolled plate；The hot rolled plate is subjected to section cooling again, hot rolled coil is coiled into after cooling；
The hot rolled coil uncoiling is cut off, pickling removes its scale on surface；The hot rolled coil is obtained cold by cold rolling
Hard volume；The chill volume uncoiling is cut off, cleaned section removes its surface and oil contaminant；The chill volume is passed through into continuous annealing treatment
Obtain strip；The strip is batched after zinc-plated, finishing as finished product.
Preferably, the heating temperature of the strand is 1230~1290 DEG C；The finishing temperature of the finish rolling is 860~900
℃；The hot rolled plate coiling temperature is 640~680 DEG C.
Preferably, when the hot rolled coil passes through cold rolling, cold rolling reduction ratio is 55-75%.
Preferably, the continuous annealing treatment, which includes annealing producing line, has rapid cooling section and annealing producing line without two kinds of sides of rapid cooling section
Formula.
Preferably, under conditions of the annealing producing line has rapid cooling section, annealing temperature is 760~780 DEG C, soaking time
50-120s, slow cooling section temperature are 695~705 DEG C, cooling rate：2.5~5 DEG C/s, 455~465 DEG C of rapid cooling section temperature, cooling rate：23~
46 DEG C/s, finishing elongation control is 0.2~0.4%.
Preferably, under conditions of the annealing producing line is without rapid cooling section, annealing temperature is 790~810 DEG C, soaking time
45-90s, slow cooling section temperature are 455~465 DEG C, cooling rate：6.7~13.5 DEG C/s, finishing elongation control is 0.3~0.5%.
One or more technical solutions provided in the embodiments of the present application have at least the following technical effects or advantages：
The present invention can be produced by rational composition design, technology controlling and process in the annealing producing line whether there is or not rapid cooling section
(in Shoudu Iron and Steel Co company standard, which requires tensile strength >=590MPa, A to the cold-rolling galvanization dual phase steel of function admirable80>=17%,
n10-20>=0.14, the actual performance index of dual phase steel provided by the invention is apparently higher than the lower limit of requirement), alloy smelting is simple,
Significantly improve production efficiency.
Further, a certain amount of chromium, molybdenum are added in dual phase steel, can be effectively improved the characteristic of austenite quenching degree, be avoided
Excessive ferritic structure is precipitated in slow cooling section.
Further, a certain amount of silicon is added in dual phase steel, carbon can be promoted to be spread into austenite, further stablizes Ovshinsky
Body.
Further, chromium, molybdenum, silicon, manganese collective effect under, austenite keep stablize, form ferrite+martensite
The finished product tissue of+a small amount of bainite.The stress strain curve of strip is in continuous yield situation, meets the mechanical property feature of dual phase steel,
Yield tensile ratio is low, and combination of strength and toughness is preferable.
Further, the defects of finishing temperature is strictly controlled in course of hot rolling, ensures austenite grain boundary in steel density increases,
Refine the rolled tissue of follow-up ferrite+pearlite.
Further, coiling temperature is strictly controlled, the uniformity of hot-rolled substrate tissue can be effectively improved, make hot-rolled substrate
Crystal grain is fine and smooth uniformly, so as to improve hot rolling banded structure, and then reduces cold rolling recrystallization crystal particle dimension so that cold rolled annealed tissue
More uniformly.
Further, cold-rolled process strictly controls annealing temperature, slow cooling section temperature, rapid cooling section temperature, to effectively control
The volume fraction of ferrite and austenite, and then martensite and ferritic ratio are controlled, and finally control the mechanical property of finished product
Energy.
Further, by cold rolling, the deformation energy storage of steel plate increases, and crystal grain is crushed, crushes, the ferrite of elongation and pearl
Body of light is interlaced, is conducive to the formation of the recrystallization softening and austenite of ferrite crystal grain, but cold rolling reduction ratio is too big, deformation
Drag increases, and increases the load of milling train, waste of energy.Cold rolling reduction ratio is 55~75%, not only improves ferrite crystal grain
The formation of recrystallization softening and austenite, and save the energy.
Further, it is strong effectively to adjust production board shape, roughness and surrender 0.2~0.5% for finishing elongation control
Degree.
Description of the drawings
It, below will be to needed in embodiment description in order to illustrate more clearly of the technical solution in the present embodiment
Attached drawing is briefly described, it should be apparent that, the accompanying drawings in the following description is one embodiment of the present of invention, for this field
For those of ordinary skill, without creative efforts, other drawings may also be obtained based on these drawings.
Fig. 1 is a kind of metallographic structure figure of Galvanized Dual Phase Steel provided in an embodiment of the present invention.
Fig. 2 is a kind of flow chart of Galvanized Dual Phase Steel production method provided in an embodiment of the present invention.
Specific implementation mode
The present invention is crucial by controlling chemical composition and smelting, rolling, annealing etc. on the basis of previous cold rolling high-strength steel
Technological parameter obtains a kind of not by the zinc-plated cold-rolling galvanization dual phase steel that the type of cooling is influenced before.
The effect of each element in the present invention：
C：Carbon is the essential element to form martensite, and carbon content determines the hardness of dual phase steel and the shape of martensite in steel
Looks；Carbon belongs to a kind of strongest solution strengthening element, and the intensity of steel can be significantly improved by increasing carbon content, meanwhile, carbon is also a kind of
Among the austenite stabilizing elements effectively improve the degree of supercooling of austenite.The weight percent content of carbon of the present invention is set as 0.085~
0.115%.
Si：Silicon is ferritic solution strengthening element, it accelerates segregation of the carbon to austenite, to the solid solution carbon in ferrite
The generation of coarse carbide, improves two-phase when having " removing " and " purification " effect, reduce gap solution strengthening and can inhibit cooling
The ductility of steel.In addition, the too high levels of silicon can influence steel plate can zinc-plated ability, for improve steel plate platability, the content of silicon is not
It is preferably excessively high.The weight percent content of silicon of the present invention is set as 0.15~0.24%.
Mn：Manganese belongs to typical austenite stabilizer element, can postpone the formation of pearlite and bainite, improves the through hardening of steel
Property, promote to form martensite in rapid cooling cooling procedure, and play the role of solution strengthening and fining ferrite grains.But manganese is moving back
It can be aoxidized and deposited in steel strip surface during fire, excessive manganese will deteriorate zinc-plated wellability, therefore the weight of manganese of the present invention
Amount degree is set as 1.45~1.55%.
P、S、N：Phosphorus, sulphur, nitrogen are impurity element.It is stringent to control in order to reduce the harmful effect to the comprehensive performance of steel
The content of phosphorus, sulphur, nitrogen in steel.The weight percent content of phosphorus of the present invention is set as≤0.015%, and the weight percent of sulphur contains
Amount is set as≤0.005%, and the weight percent content of nitrogen is set as≤0.006%.
Alt：Aluminium belongs to closing austenite phase p-block element p, can expand the two-phase section of ferrite and austenite, increases at heat
The flexibility of science and engineering skill helps to maintain the stability and reproducibility of two-phase Steel Properties.In addition, aluminium can play certain refinement
Crystal grain invigoration effect can also promote Carbon diffusion in ferrite, effectively purify ferrite.The weight percent of aluminium of the present invention contains
Amount is set as 0.025~0.065%.
Cr：Chromium is middle carbide, can significantly improve the quenching degree of steel, can postpone strongly perlitic transformation and
Bainite transformation.Though chromium is weak solution strengthening element, the supercooling ability of austenite can be increased, to thinning microstructure, obtained by force
Change effect.The weight percent content of chromium of the present invention is set as 0.14~0.24%.
Mo：Molybdenum belongs to middle carbide, is formed by the quenching degree of austenite when the heating of critical zone to improving
With desirable influence, at the same molybdenum to the inhibiting effect of perlitic transformation clearly, in order to improve the quenching degree of steel, together
When inhibit to be quickly cooled down the formation of the tissues such as process medium pearlite.The weight percent content of molybdenum of the present invention is set as 0.24~
0.29%.
A certain amount of chromium is added in Galvanized Dual Phase Steel, molybdenum is to improve the characteristic of austenite quenching degree, avoid slow cooling section
Excessive ferritic structure is precipitated.In addition, the stable austenite when strip is in middle thermophase, reduces austenite decomposition Cheng Tiesu
Body+carbide (bainite structure).A certain amount of silicon is added in ingredient, since silicon has " purification " ferritic effect, can be incited somebody to action
The carbon dissolved in ferrite arranges the stability that remaining austenite is further improved to remaining austenite.In chromium, molybdenum, silicon, manganese
Under collective effect, in 460 DEG C of middle warm area, austenite is stablized, and a large amount of austenites occur for the air-cooled stage after zinc-plated to geneva
The transformation of body phase transformation forms the tissue of ferrite+martensite+a small amount of bainite.The presence of a small amount of bainite, in aspect of performance
Apparent influence is not generated, and the stress strain curve of strip is in continuous yield situation, meets the mechanical property feature of dual phase steel, yield tensile ratio
Low, combination of strength and toughness is preferable.
The present invention is vertical continuous using 2250mm hot tandems, 2030mm coupled pickling and tandem mills and 1550mm or 2030mm
Annealing furnace unit.
Technological process is：KR desulfurization process, conventional pneumatic steelmaking, LF+RH refining treatments, RH Calcium treatments, continuous casting, steel billet add
Heat, finish rolling, section cooling, is batched at roughing；Uncoiling, cold continuous rolling, is batched at pickling；Uncoiling, cleaning, annealing, zinc-plated, finishing, volume
It is bent.
The smelting process of strand is：Molten iron is by KR desulfurization pretreatments, conventional converter smelting, LF+RH refining treatments, RH calcium
Processing accurately controls the chemical composition of molten steel, then conticaster is utilized to obtain required strand.
Hot rolling technology is：First by 1230~1290 DEG C of heating strand, heating time is 3~3.5 hours；By fixed width pressure
Power obtains required strand width；Using de-scaling, two roller roughing and four-roller roughing；Using mm finishing mill unit；Section cooling
After batch.The defects of strictly controlling finishing temperature and coiling temperature in course of hot rolling, ensureing austenite grain boundary in steel density increases,
The rolled tissue of follow-up ferrite+pearlite is refined, the stringent finishing temperature that controls is 860~900 DEG C, coiling temperature 640
~680 DEG C.
Cold-rolling process is：Hot rolled coil uncoiling is cut off, entering descaling bath by straightening scale breading removes its scale on surface,
Subsequently into 5 Stands Cold Tandem Mill groups roll, reduction ratio be 55~75%, after batch as chill volume；Chill volume is being annealed again
Inlet uncoiling cuts off feeding, and cleaned section removes its surface and oil contaminant and enter vertical annealing furnace, zinc-plated, air-cooled, using finishing
It is batched after machine rolling.Annealing process strictly controls heating temperature, slow cooling temperature, rapid cooling temperature and finishing elongation percentage.In slow cooling section
With the continuous annealing unit of rapid cooling Duan Junyou, ensure that bringing-up section temperature is 760~780 DEG C, 50~120s of soaking time, slow cooling section temperature
For 695~705 DEG C, cooling rate：2.5~5 DEG C/s, rapid cooling section temperature is 455~465 DEG C, cooling rate：23~46 DEG C/s, finishing extends
Rate is controlled 0.2~0.4%.In continuous annealing unit of the only slow cooling section without rapid cooling section, ensure bringing-up section temperature be 790~810 DEG C,
45~90s of soaking time, slow cooling section temperature are 455~465 DEG C, cooling rate：6.7~13.5 DEG C/s, finishing elongation control is 0.3
~0.5%.
Embodiment 1
Molten iron is passed through into KR desulfurization process, conventional converter smelting, LF+RH refining treatments, RH Calcium treatments, carries out continuous casting again；
Strand smelting component is：C：0.095%, Si：0.15%, Mn：1.50%, P：0.010%, S：0.003%, Alt：0.035%,
Cr：0.20%, Mo：0.29%, N：0.003%, remaining is iron and other inevitable impurity.
1270 DEG C of heating strand, heating time are 3.1 hours, and finishing temperature is 880 DEG C, and coiling temperature is 660 DEG C；Then
Enter 5 rack cold continuous rollings after removing its scale on surface into shallow slot turbulence acid dip after the broken phosphorus of uncoiling straightening on sour rolling mill
Machine, reduction ratio 65%；Enter vertical annealing furnace after the last uncoiling of annealing unit inlet, cleaning, bringing-up section temperature is 770
DEG C, soaking time 80s, slow cooling section outlet temperature be 700 DEG C, cooling rate：3.5 DEG C/s, rapid cooling section outlet temperature be 460 DEG C, it is cold
Speed：It is 23 DEG C/s, then zinc-plated into zinc pot, go out that zinc pot is air-cooled, using 0.3% finishing, curling, it is 1.5mm to produce specification
The DP600+Z of × 1580mm.Its yield strength is 395MPa, tensile strength 625MPa, elongation after fracture A80It is 22%,
n10-20Value is 0.17.
Embodiment 2
Molten iron is passed through into KR desulfurization process, conventional converter smelting, LF+RH refining treatments, RH Calcium treatments, carries out continuous casting again；
Strand smelting component is：C：0.110%, Si：0.24%, Mn：1.45%, P：0.010%, S：0.004%, Alt：0.055%,
Cr：0.16%, Mo：0.27%, N：0.003%, remaining is iron and other inevitable impurity.
1260 DEG C of heating strand, heating time are 3.2 hours, and finishing temperature is 880 DEG C, and coiling temperature is 670 DEG C；Then
Enter 5 rack cold continuous rollings after removing its scale on surface into shallow slot turbulence acid dip after the broken phosphorus of uncoiling straightening on sour rolling mill
Machine, reduction ratio 75%；Enter vertical annealing furnace after the last uncoiling of annealing unit inlet, cleaning, bringing-up section temperature is 800
DEG C, soaking time 80s, slow cooling section outlet temperature be 460 DEG C, cooling rate：10 DEG C/s, then zinc-plated into zinc pot, it is air-cooled to go out zinc pot, then
By 0.4% finishing, the DP600+Z that specification is 0.85mm × 859mm is produced in curling.Its yield strength is 363MPa, resists
Tensile strength is 650MPa, elongation after fracture A80For 23%, n10-20Value is 0.17.
Embodiment 3
Molten iron is passed through into KR desulfurization process, conventional converter smelting, LF+RH refining treatments, RH Calcium treatments, carries out continuous casting again；
Strand smelting component is：C：0.115%, Si：0.22%, Mn：1.50%, P：0.012%, S：0.004%, Alt：0.025%,
Cr：0.15%, Mo：0.26%, N：0.002%, remaining is iron and other inevitable impurity.
1230 DEG C of heating strand, heating time are 3.2 hours, and finishing temperature is 860 DEG C, and coiling temperature is 660 DEG C；Then
Enter 5 rack cold continuous rollings after removing its scale on surface into shallow slot turbulence acid dip after the broken phosphorus of uncoiling straightening on sour rolling mill
Machine, reduction ratio 65%；Enter vertical annealing furnace after the last uncoiling of annealing unit inlet, cleaning, bringing-up section temperature is 760
DEG C, soaking time 60s, slow cooling section outlet temperature be 700 DEG C, cooling rate：5.0 DEG C/s, rapid cooling section outlet temperature be 460 DEG C, it is cold
Speed：It is 23 DEG C/s, then zinc-plated into zinc pot, go out that zinc pot is air-cooled, using 0.4% finishing, curling, it is 1.5mm to produce specification
The DP600+Z of × 1580mm.Its yield strength is 400MPa, tensile strength 645MPa, elongation after fracture A80It is 25%,
n10-20Value is 0.17.
Embodiment 4
Molten iron is passed through into KR desulfurization process, conventional converter smelting, LF+RH refining treatments, RH Calcium treatments, carries out continuous casting again；
Strand smelting component is：C：0.085%, Si：0.17%, Mn：1.45%, P：0.013%, S：0.003%, Alt：0.025%,
Cr：0.18%, Mo：0.29%, N：0.004%, remaining is iron and other inevitable impurity.
1290 DEG C of heating strand, heating time are 3.0 hours, and finishing temperature is 900 DEG C, and coiling temperature is 680 DEG C；Then
Enter 5 rack cold continuous rollings after removing its scale on surface into shallow slot turbulence acid dip after the broken phosphorus of uncoiling straightening on sour rolling mill
Machine, reduction ratio 70%；Enter vertical annealing furnace after the last uncoiling of annealing unit inlet, cleaning, bringing-up section temperature is 810
DEG C, soaking time 90s, slow cooling section outlet temperature be 465 DEG C, cooling rate：10 DEG C/s, then zinc-plated into zinc pot, it is air-cooled to go out zinc pot, then
By 0.5% finishing, the DP600+Z that specification is 0.85mm × 859mm is produced in curling.Its yield strength is 385MPa, resists
Tensile strength is 665MPa, elongation after fracture A80For 23%, n10-20Value is 0.18.
Embodiment 5
Molten iron is passed through into KR desulfurization process, conventional converter smelting, LF+RH refining treatments, RH Calcium treatments, carries out continuous casting again；
Strand smelting component is：C：0.097%, Si：0.15%, Mn：1.48%, P：0.010%, S：0.003%, Alt：0.055%,
Cr：0.24%, Mo：0.28%, N：0.004%, remaining is iron and other inevitable impurity.
1250 DEG C of heating strand, heating time are 3.1 hours, and finishing temperature is 860 DEG C, and coiling temperature is 640 DEG C；Then
Enter 5 rack cold continuous rollings after removing its scale on surface into shallow slot turbulence acid dip after the broken phosphorus of uncoiling straightening on sour rolling mill
Machine, reduction ratio 55%；Enter vertical annealing furnace after the last uncoiling of annealing unit inlet, cleaning, bringing-up section temperature is 770
DEG C, soaking time 100s, slow cooling section outlet temperature be 705 DEG C, cooling rate：4.5 DEG C/s, rapid cooling section outlet temperature be 465 DEG C, it is cold
Speed：It is 30 DEG C/s, then zinc-plated into zinc pot, go out that zinc pot is air-cooled, using 0.3% finishing, curling, it is 1.5mm to produce specification
The DP600+Z of × 1580mm.Its yield strength is 415MPa, tensile strength 665MPa, elongation after fracture A80It is 24%,
n10-20Value is 0.17.
A kind of Galvanized Dual Phase Steel provided in an embodiment of the present invention and its production method include at least following technique effect：
1, the present invention can be produced by rational composition design, technology controlling and process in the annealing producing line whether there is or not rapid cooling section
Go out the cold-rolling galvanization dual phase steel of function admirable, alloy smelting is simple, significantly improves production efficiency.
2, a certain amount of chromium, molybdenum are added in dual phase steel, can effectively improve the characteristic of austenite quenching degree, slow cooling section is avoided to analyse
Go out excessive ferritic structure.
3, a certain amount of silicon is added in dual phase steel, silicon can promote carbon to be spread into austenite, further stable austenite.
4, chromium, molybdenum, silicon, manganese collective effect under, austenite keep stablize, form ferrite+martensite+a small amount of shellfish
The finished product tissue of family name's body.The stress strain curve of strip is in continuous yield situation, meets the mechanical property feature of dual phase steel, yield tensile ratio
Low, combination of strength and toughness is preferable.
5, the defects of strictly controlling finishing temperature in course of hot rolling, ensureing austenite grain boundary in steel density increases, after refinement
The rolled tissue of continuous ferrite, pearlite.
6, coiling temperature is strictly controlled, the uniformity of hot-rolled substrate tissue can be effectively improved, keeps the crystal grain of hot-rolled substrate thin
It is greasy uniform, so as to improve hot rolling banded structure, and then reduce cold rolling recrystallization crystal particle dimension so that cold rolled annealed tissue is more equal
It is even.
7, cold-rolled process strictly controls annealing temperature, slow cooling section temperature, rapid cooling section temperature, effectively controls ferrite and Austria
The volume fraction of family name's body, and then martensite and ferritic ratio are controlled, and finally control the mechanical property of finished product.
8, by cold rolling, the deformation energy storage of steel plate increases, and crystal grain is crushed, crushes, ferrite and the pearlite phase of elongation
Mutually staggeredly, be conducive to the formation of the recrystallization softening and austenite of ferrite crystal grain, but cold rolling reduction ratio is too big, resistance of deformation increases
Greatly, the load of milling train, waste of energy are increased.Cold rolling reduction ratio is 55~75%, not only improves the recrystallization of ferrite crystal grain
Refinement and the formation of austenite, and save the energy.
9, finishing elongation control effectively adjusts production board shape, roughness and yield strength 0.2~0.5%.
It should be noted last that the above specific implementation mode is merely illustrative of the technical solution of the present invention and unrestricted,
Although being described the invention in detail with reference to example, it will be understood by those of ordinary skill in the art that, it can be to the present invention
Technical solution be modified or replaced equivalently, without departing from the spirit of the technical scheme of the invention and range, should all cover
In the scope of the claims of the present invention.
Claims (6)
1. a kind of method of Galvanized Dual Phase Steel, which is characterized in that the component and weight percent content of the dual phase steel be：C：
0.085~0.115%, Si：0.15~0.24%, Mn：1.45~1.55%, P：≤ 0.015%, S：≤ 0.005%, Alt：
0.025~0.065%, Cr：0.14~0.24%, Mo：0.24~0.29%, N：≤ 0.006%, remaining can not with other for iron
Avoid impurity；
Wherein, the yield strength of the Galvanized Dual Phase Steel is 350~425MPa, and tensile strength is 600~670MPa；It is described zinc-plated
The width of dual phase steel is 1000~1860mm, and thickness is 0.3~2.5mm, the elongation after fracture A of the Galvanized Dual Phase Steel80It is 22
~27%, n10-20Value is 0.16~0.18；
The method includes：
Molten iron is obtained into strand by KR desulfurization pretreatments, converter smelting, LF+RH refining treatments, RH Calcium treatments, continuous casting；
The strand is heated；By fixed width pressure, required strand width is obtained；Heat is obtained by roughing, finish rolling
Roll plate；The hot rolled plate is subjected to section cooling again, hot rolled coil is coiled into after cooling；
The hot rolled coil uncoiling is cut off, pickling removes its scale on surface；The hot rolled coil obtains chill volume by cold rolling；
The chill volume uncoiling is cut off, cleaned section removes its surface and oil contaminant；The chill volume is obtained by continuous annealing treatment
Strip；The strip is batched after zinc-plated, finishing as finished product.
2. producing a kind of method of Galvanized Dual Phase Steel as described in claim 1, it is characterised in that：The heating temperature of the strand
It is 1230~1290 DEG C；The finishing temperature of the finish rolling is 860~900 DEG C；The hot rolled plate coiling temperature is 640~680 DEG C.
3. producing a kind of method of Galvanized Dual Phase Steel as described in claim 1, it is characterised in that：The hot rolled coil passes through cold rolling
When, cold rolling reduction ratio is 55-75%.
4. producing a kind of method of Galvanized Dual Phase Steel as described in claim 1, it is characterised in that：The continuous annealing treatment packet
Including annealing producing line has rapid cooling section and annealing producing line without rapid cooling section two ways.
5. producing a kind of method of Galvanized Dual Phase Steel as claimed in claim 4, it is characterised in that：Have soon in the annealing producing line
Under conditions of cold section, annealing temperature be 760~780 DEG C, soaking time 50-120s, slow cooling section temperature be 695~705 DEG C, it is cold
Speed：2.5~5 DEG C/s, 455~465 DEG C of rapid cooling section temperature, cooling rate：23~46 DEG C/s, finishing elongation control 0.2~
0.4%.
6. producing a kind of method of Galvanized Dual Phase Steel as claimed in claim 4, it is characterised in that：In the annealing producing line without fast
Under conditions of cold section, annealing temperature is 790~810 DEG C, soaking time 45-90s, and slow cooling section temperature is 455~465 DEG C, cooling rate：
6.7~13.5 DEG C/s, finishing elongation control is 0.3~0.5%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610439055.1A CN106086638B (en) | 2016-06-17 | 2016-06-17 | A kind of Galvanized Dual Phase Steel and its production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201610439055.1A CN106086638B (en) | 2016-06-17 | 2016-06-17 | A kind of Galvanized Dual Phase Steel and its production method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106086638A CN106086638A (en) | 2016-11-09 |
| CN106086638B true CN106086638B (en) | 2018-08-21 |
Family
ID=57236464
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610439055.1A Active CN106086638B (en) | 2016-06-17 | 2016-06-17 | A kind of Galvanized Dual Phase Steel and its production method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106086638B (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106755867B (en) * | 2016-12-01 | 2019-01-18 | 首钢集团有限公司 | A kind of hot dip galvanized dual phase steel surface treatment method |
| CN106623430B (en) * | 2016-12-02 | 2018-10-19 | 首钢集团有限公司 | A method of eliminating Galvanized Dual Phase Steel rough surface defect |
| CN106676392B (en) * | 2016-12-27 | 2019-02-22 | 首钢集团有限公司 | Heat zinc coating plate and its production method |
| CN107971338A (en) * | 2017-11-23 | 2018-05-01 | 攀钢集团攀枝花钢铁研究院有限公司 | The high-strength chill volume cold rolling process of building concrete fixing piece |
| CN108559901A (en) * | 2018-05-31 | 2018-09-21 | 攀钢集团西昌钢钒有限公司 | A kind of dual phase steel and its smelting process and the method for reducing nitrogen content in dual phase steel |
| CN109465295B (en) * | 2018-08-06 | 2020-06-09 | 首钢集团有限公司 | Method for preventing edge cracking and strip breakage of hot continuous rolled steel plate in cold rolling |
| CN111041341A (en) * | 2018-10-11 | 2020-04-21 | 鞍钢广州汽车钢有限公司 | High-strength dual-phase steel formula and zinc plating production process thereof |
| CN109852900B (en) * | 2019-03-29 | 2021-07-30 | 山东钢铁集团日照有限公司 | 600 MPa-grade hot-galvanized dual-phase steel with different yield ratios and production method thereof |
| CN110578042B (en) * | 2019-10-18 | 2021-03-30 | 山东钢铁集团日照有限公司 | Production method of steel for cold-hardening pipe |
| 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 |
| CN112048670B (en) * | 2020-09-07 | 2021-12-24 | 鞍钢股份有限公司 | Cold-rolled hot-galvanized DH590 steel with excellent surface quality and production method thereof |
| CN114369707B (en) * | 2021-12-03 | 2024-02-06 | 首钢集团有限公司 | Strip steel without flat coil defect and chromatic aberration defect, and preparation method and application thereof |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100507053C (en) * | 2004-11-29 | 2009-07-01 | 宝山钢铁股份有限公司 | 800MPa cold rolled and hot zinc plated double phase steel and its producing method |
| KR100958019B1 (en) * | 2009-08-31 | 2010-05-17 | 현대하이스코 주식회사 | Dual phase steel sheet and method for manufacturing the same |
| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| CN103627953B (en) * | 2013-12-12 | 2016-04-27 | 首钢总公司 | A kind of insensitive containing aluminium Multiphase Steel and production method thereof to isothermal time |
| CN104831177B (en) * | 2015-05-11 | 2017-11-17 | 首钢总公司 | A kind of cold-rolled galvanized duplex steel and preparation method thereof |
-
2016
- 2016-06-17 CN CN201610439055.1A patent/CN106086638B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN106086638A (en) | 2016-11-09 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106086638B (en) | A kind of Galvanized Dual Phase Steel and its production method | |
| CN102586688B (en) | A kind of dual phase sheet steel and manufacture method thereof | |
| CN104928457A (en) | Method for producing high-ductility ferritic stainless steel band through furnace roll and continuous mill | |
| CN112538593B (en) | Hot dip galvanizing IF steel plate production method capable of controlling surface waviness | |
| CN110578042B (en) | Production method of steel for cold-hardening pipe | |
| JPS58144430A (en) | Manufacture of cold-rolled steel sheet excellent in press-workability | |
| CN105483549A (en) | High-strength cold-rolled steel plate for wide and thin automobile and production method thereof | |
| CN109295283A (en) | A kind of method that short annealing prepares 1000MPa grades of high ductile steels | |
| CN110551939A (en) | Hot-dip galvanized steel plate with yield strength of 320MPa and production method thereof | |
| CN110964969B (en) | High-strength hot-dip galvanized quenching distribution steel and production method thereof | |
| CN110592348A (en) | Ultra-low carbon cold rolled steel performance grading control method | |
| CN107815591A (en) | Hot-dip galvanizing sheet steel and preparation method thereof | |
| CN111041166A (en) | Cold-rolled steel plate for automobile silencing sheet and production method thereof | |
| CN100469935C (en) | CSP production process for hot-galvanizing-baking hardened steel sheet | |
| CN112795731A (en) | Cold-rolled steel plate for lampshade and production method thereof | |
| CN110904392A (en) | Ultra-low carbon anti-pressure thin-specification cold-rolled sheet for battery shell and production method thereof | |
| CN113215484B (en) | Phase-change induced plasticity steel and preparation method and application thereof | |
| CN108998730A (en) | Hypereutectoid tool steel and manufacturing method thereof | |
| CN112063818A (en) | Low-temperature coiled cold-rolled steel plate with high formability and production method thereof | |
| CN102676913B (en) | Cold-rolled steel strip for flux-cored wire and production method of cold-rolled steel strip | |
| CN103627953B (en) | A kind of insensitive containing aluminium Multiphase Steel and production method thereof to isothermal time | |
| CN110358976A (en) | High-carbon steel thin strip and production method thereof | |
| CN113151651B (en) | Production method of low-temperature annealed ultra-deep drawn cold-rolled steel plate and cold-rolled steel plate | |
| JP3997692B2 (en) | Manufacturing method of cold-rolled steel sheet for deep drawing with excellent press-formability and less fluctuation of press-formability in the coil | |
| CN106282818B (en) | The cold rolling coil that 980MPa grades of tensile strength banding steel and its manufacturing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| CB02 | Change of applicant information |
Address after: 100041 Shijingshan Road, Beijing, No. 68, No. Applicant after: Shougang Group Co. Ltd. Address before: 100041 Shijingshan Road, Beijing, No. 68, No. Applicant before: Capital Iron & Steel General Company |
|
| CB02 | Change of applicant information | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |