CN108796375A - A kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels and its minimizing production method - Google Patents
A kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels and its minimizing production method Download PDFInfo
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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- 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
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Abstract
Include following component the present invention relates to a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels and its minimizing production method, the hot-dip galvanized high-strength steel：C：0.06~0.18%, Mn：1.60~2.50%, Als：0.005~0.050%, Si：0.10~0.50%, V：0.20~0.40%, P：≤ 0.015%, S：≤ 0.010%, N：≤ 0.008%, product microstructure is mainly made of 85~95% ferrites, 0~10% bainite, 0~10% martensite, and in steel≤the precipitate percent by volume of 10nm is 0.2~1%.Its production method is：Steel-making, refining, continuous casting hot rolling, pickling, zinc-plated, finishing of annealing eliminate the cold rolling process of traditional processing technology flow, production procedure is significantly shortened, production process energy consumption and CO2Discharge can substantially reduce, and production efficiency is obviously improved.
Description
Technical field
The present invention relates to galvanizing super-high strength steel manufacturing technology fields, are related to a kind of tensile strength 1000MPa grades of galvanizings
High-strength steel and its minimizing production method.
Background technology
In recent years, in order to reduce the energy consumption during automobile use, CO is reduced2Discharge, automobile steel etc. is just towards thin and thick
Metric lattice, high-strength direction are developed, and 1000MPa grades or more of super-high strength steel is one of its main direction of development.With it is common cold
High-strength steel is rolled to compare, zinc coated high strength steel not only with high intensity, also with good corrosion resistance, therefore 1000MPa with
The upper zinc-plated super-high strength steel of rank is used widely.
In the prior art, the microstructure of 1000MPa grades of zinc-plated super-high strength steels be mainly 15~60% ferrite and
30~80% martensites, bainite and retained austenite, intensity mainly by promotions such as bainite, martensites in steel, manufacture work
Skill flow is conventional process flow, i.e. steel-making → continuous casting → hot rolling → pickling → cold rolling → annealing is zinc-plated, is rolled in cold rolling process
Difficulty, production procedure is long, and energy consumption and emission problem protrude, and due to the alloy content of high-strength steel height, there is rolling in cold rolling
The problems such as load is big, plate shape is difficult to control, rolling crack.CN103805840A discloses a kind of high formability galvanizing super-high strength steel
Plate and its manufacturing method, main chemical compositions C：0.15~0.25%, Si：1.00~2.00%, Mn：1.50~3.00%,
P：≤ 0.015%, S：≤ 0.012%, Al：0.03-0.060%, N：≤ 0.008%, remaining is Fe and inevitable impurity
Element.Microstructure is made of 10~30% ferrites and 60~80% martensites and 5~15% retained austenites, product surrender
600~900MPa of intensity, 980~1200MPa of tensile strength, elongation percentage 15~22%.Production stage includes through smelting, being cast into
Slab, heating, hot rolling, cold rolling after pickling, annealing, 1170~1230 DEG C of slab heating temperature, 850~910 DEG C of finishing temperature, volume
550~650 DEG C of temperature is taken, cold-rolling deformation rate 40~60%, annealing is using straight fiery heated oxide atmosphere and radiation mode also Primordial Qi
Atmosphere heats two sections of heating, wherein straight fire heating is heated to 680~750 DEG C in oxidizing atmosphere, dew point in continuous annealing furnace >=-
35 DEG C, then it is heated to 840~920 DEG C in reducing atmosphere with radiation mode, and 40~80s is kept the temperature, control H content in stove
8%~15%, then with the cooling rate slow cooling of 3~10 DEG C/s to 720~800 DEG C, then it is cooled to 260~360 DEG C soon, cooling rate >=
It 50 DEG C/s, converts the austenite to for martensite, then be again heated to 460~470 DEG C, keeps the temperature 60~120s.CN 102348821A
Disclose the high-strength hot-dip zinc-coated steel sheet having excellent moldability and its manufacturing method, main chemical compositions C：0.05~0.20%,
Si：0.50~2.50%, Mn：1.50~3.0%, P：0.001~0.05%, S：0.0001~0.01%, Al：0.001~
0.10%, N：0.0005~0.01%, Cr：0.01~1.5%, Ti：0.0005~0.10%, B：0.0003~0.003%,
Nb：0.005~0.05%, Mo：0.01~1.0%, Ni：0.01~2.0%, Cu：0.01~2.0%, remaining is Fe and can not
The impurity element avoided.Production technology includes that mentioned component is heated to 1150~1300 DEG C, then in 800~950 DEG C of finish to gauges,
Then cold rolling is carried out with 40% or more reduction ratio with the heating speed of 5 DEG C/s to AC1~AC3, and to be kept the temperature, so later
It anneals afterwards at 600 DEG C or less, and carries out zinc layers Alloying Treatment at 450~600 DEG C.Product tensile strength can reach 900
~1200MPa, elongation percentage 14~22%, hole expansibility reach 50% or more, and the ratio between 90 ° of bending radius and thickness are less than 0.40.On
Method existing cold rolling difficulty when producing 1000MPa grades of zinc-plated super-high strength steels is stated, rolling load is big, production procedure is long,
Energy consumption is big and CO2Discharge distinct issues, it would be highly desirable to solve.
Invention content
It is a kind of without cold the technical problem to be solved by the present invention is to aiming at the above shortcomings existing in the prior art, provide
The ingredient and its minimizing manufacturing method of the super high strength steel of 1000MPa grades of process are rolled, the product of production has good power
Learn performance, forming property and surface quality.
In order to solve the above technical problems, technical solution provided by the invention is：
A kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels are provided, the hot-dip galvanized high-strength steel includes following weight hundred
Divide the chemical composition of ratio：C：0.06~0.18%, Mn：1.60~2.50%, Als：0.005~0.050%, Si：0.10~
0.50%, V：0.20~0.40%, P：≤ 0.015%, S：≤ 0.010%, N：≤ 0.008%, remaining is for Fe and unavoidably
Impurity, product microstructure is mainly made of 85~95% ferrites, 0~10% bainite, 0~10% martensite, and steel
In≤the precipitate percent by volume of 10nm is 0.2~1%.
By said program, the chemical composition further includes at least one of Nb, Ti, Cr, Mo, B element, shared by each element
Mass percent is：Nb：0.005~0.050%, Ti：0.005~0.15%, Cr：0.05~0.30%, Mo：0.05~
0.50%, B：0.0005~0.003%.
The present invention also provides the minimizing production methods of above-mentioned tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, specific to wrap
Include following steps：Steel-making, refining, continuous casting hot rolling, pickling, zinc-plated, finishing of annealing；
The continuous casting hot-rolled step is：Continuous casting, heating, roughing, finish rolling is cooling, batches, wherein heating temperature be 1150~
1300 DEG C, roughing temperature is 900~1300 DEG C, roughing reduction ratio >=80%, and final rolling temperature is 850~950 DEG C, finish rolling reduction ratio
>=70%, in cooling procedure at 650 DEG C or more, average cooling rate >=20 DEG C/s is batched in 200~600 DEG C of completions；Or
The continuous casting hot-rolled step is：Continuous casting, roughing, heating, finish rolling is cooling, batches, and wherein roughing temperature is 900 DEG C
More than, then roughed bloom is heated to 900~1200 DEG C by roughing reduction ratio >=80%, finish rolling, finish rolling are completed at 850~950 DEG C
Reduction ratio >=70%, in cooling procedure at 650 DEG C or more, average cooling rate >=20 DEG C/s completes volume at 200~600 DEG C
It takes；Or
The continuous casting hot-rolled step is：Continuous casting, heating, finish rolling is cooling, batches, and wherein heating temperature is 1150~1300
DEG C, complete finish rolling at 850~950 DEG C, finish rolling reduction ratio >=90%, in cooling procedure at 650 DEG C or more, average cooling rate
It >=20 DEG C/s, is batched in 200~600 DEG C of completions.
By said program, the zinc-plated step of the annealing include strip heating, soaking, cooling, it is zinc-plated, plate postcooling, wherein
550~840 DEG C, 30~200s of soaking time of soaking temperature, cooling rate >=15 DEG C/s in cooling procedure, strip in galvanizing process
Enter 440~500 DEG C of zinc pot temperature, 450~470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15~0.25%, dew point-in annealing furnace
20~-50 DEG C, hydrogen content is 1~10% in stove, residual oxygen≤30ppm.
By said program, the zinc-plated step of annealing includes strip heating, soaking, cooling, zinc-plated, plating postcooling, Re Chu
Reason, plating postcooling, wherein 550~840 DEG C of soaking temperature, 30~200s of soaking time, soaking to zinc-plated cooling rate >=15
DEG C/s, strip enters 440~500 DEG C of zinc pot temperature, 450~470 DEG C of zinc liquid temperature, heat treatment temperature 500~600 in galvanizing process
DEG C, plating postcooling rate >=8 DEG C/s, zinc liquid aluminium content 0.15~0.25%, dew point -20~-50 DEG C in annealing furnace, hydrogen in stove
Content is 1~10%, residual oxygen≤30ppm.
By said program, the finishing step finishing reduction ratio 0.1~1%.
Prepared by the present invention eliminates cold rolling step and prior art during hot-dip galvanized high-strength steel there are marked difference,
It is redesigned on ingredient, and is improved in technique and solves the problems, such as to remove cold-rolled strip, mainly in continuous casting hot rolling
Zinc-plated stage uses above-mentioned several schemes with annealing, provide and after cold rolling same thickness raw material.
The effect of each element and main technique in the present invention：
C：Carbon plays solution strengthening effect in steel, or with carbide formers such as Nb, Ti, Mo in steel to form MC tiny
Particle plays the role of precipitation strength and crystal grain thinning, improves the intensity of steel.Excessively high carbon content reduces the weldability of steel
Can, therefore consider, the C content in steel is selected as 0.06%~0.18%.
Mn：Mn plays solution strengthening and stable austenite in steel, improves quenching degree, and content is too low, invigoration effect
Too small, austenite is unstable.Mn too high levels are easy to form macrosegregation in strip mid-depth, reduce toughness of products, cause
Molding cracking, while Mn too high levels, the cost of alloy of product dramatically increase, thus Mn contents of the present invention for 1.60~
2.50%.
Si：Si is solution strengthening element, is remarkably improved the intensity of steel, but Si is easy to aoxidize, and in steel surface richness
Collection, impacts the surface quality of product, and particularly with hot-dip galvanized high-strength steel, the content of Si should not be too high, therefore the present invention
Middle Si contents are 0.01~0.50%.
Al：Al is easy to combine with the N in steel, forms the precipitates such as AlN, the free N content in steel is made to reduce, and reduces in steel
The consumption of other microalloy V, Nb, Ti promote the precipitation of tiny VC, Nb, TiC particle in steel, but Al content is too high, are easily formed thick
Big AlN particles reduce the toughness of steel, therefore Al content is 0.005~0.05% in the present invention.
P：P is the impurity element in steel, is easy to influence the toughness of product in crystal boundary segregation, therefore the lower its content the better,
According to practical controlled level, should control below 0.015%.
S：S is the impurity element in steel, easily generates segregation in crystal boundary, and form the FeS of low melting point with the Fe in steel, reduces
The toughness of steel, when steel-making, should fully remove, and should control 0.010%.
N：N is the impurity element in steel, reduces the toughness of steel, is easy and the shapes nitride grains such as Al, Nb, Ti, V, B in steel
Son, too high levels, the easy toughness for forming coarse precipitates and reducing steel, therefore its content is reduced as possible, it should control
0.006% or less.
V：V is main microalloy element in the present invention, and V is easy to combine with C, N in steel in steel, at a lower temperature
It is precipitated, forms the fine particles such as nano level VC, improve the intensity of steel, but V is too high, so that manufacturing cost is increased, therefore this hair
The content of bright V is 0.20~0.40%.
Nb：Nb can significantly refine ferrite crystal grain in steel, improve the intensity and toughness of steel, also first with C, N in steel etc.
Element forms the particles such as NbC, NbN, plays the role of precipitation strength, improves steel strength, but Nb too high levels can increase steel
Manufacturing cost, therefore the content of Nb is 0.005~0.050% in the present invention.
Ti：Ti is combined to form TiC and TiN with C, N in steel, plays the role of precipitation strength, but Ti is also easily combined with N,
It is precipitated in molten steel, forms coarse TiN particles, reduce the toughness of steel, and Ti too high levels bring cost to increase, therefore this
The content of Ti is 0.005~0.150% in invention.
Cr：Cr is remarkably improved the quenching degree of steel, and has the function of inhibiting Carbide Precipitation and perlitic transformation, has
Conducive to promoting the formation of bainite and martensite in steel, but the too high increase cost of content, therefore Cr contents are 0.05 in the present invention
~0.30%.
Mo：Mo is remarkably improved the quenching degree of steel, and the transformation of steel cryo tissue bainite and martensite, Mo is promoted to contain
The excessively high manufacturing cost that can dramatically increase steel is measured, therefore the content of Mo is 0.05~0.30% in the present invention.
B：B has the function of improving austenite quenching degree, effectively facilitates the formation of martensite in steel, combined with the N in steel
BN is formed, precipitation strength is played the role of, B is easy to be enriched in austenite grain boundary, inhibits ferritic transformation, B content is excessively high to be made
Steel degraded toughness, and the manufacturing cost of steel can be increased, therefore the content of B is 0.0005~0.0050% in the present invention.
Main technique reason in the present invention is analyzed as follows：
Slab heating temperature uses 1150-1300 DEG C, and it is uniform that board briquette less than 1150 DEG C is unfavorable for alloying element in steel
Change, cause ingredient and microstructure segregation, and be unfavorable for V, Nb, Ti for being precipitated in continuous casting cooling procedure carbonitride it is again solid
Molten, heating temperature is higher than 1300 DEG C, and surface is easy to form the iron scale for being difficult to remove, and product surface quality is made to be deteriorated.
In hot rolling rough rolling process, roughing temperature is too low, and rolling equipment rolling load increases, and steel strip shape quality is deteriorated, because
This should complete roughing at 900 DEG C or more, and roughing reduction ratio is too low, is unfavorable for crystal grain refinement, causes tissue coarse, reduces product
Intensity and toughness.
Finishing temperature is relatively low in course of hot rolling is easy to form non-uniform tissue in steel, and it is higher be easy to be formed it is coarse
Grain structure is unfavorable for the mechanical property of product, therefore 850~950 DEG C of hot rolling finishing temperature of the present invention.Finish rolling reduction ratio is too
It is low to be unfavorable for crystal grain refinement, easily form coarse grain structure.
In cooling procedure after hot rolling, less than 20 DEG C/s it is easy to be precipitated in steel in 650 DEG C or more of cooling velocities coarse
Uneven ferritic structure and microalloy carbide, cause the toughness indexs such as the performance especially elongation percentage of product decline.
In coiling process, coiling temperature is excessively high, be easy to cause to form coarse ferrite and coarse carbide is precipitated
Particle, and coiling temperature is too low, is easy to cause deformed steel strip, thus in the present invention coiling temperature at 200~600 DEG C.
During continuous annealing, it is covered with zinc in order to make belt steel surface that can uniformly apply, therefore annealing temperature is greater than 450
DEG C, optimal 550 DEG C or more, annealing temperature is too high, is easy to form coarse heterogeneous structure and VC precipitates, and is easy to facilitate table
Face external oxidation, it is unfavorable to final paintability, therefore 550~840 DEG C of annealing temperature of the present invention.
Soaking time when annealing is too short, and sufficient Recovery and recrystallization cannot occur for cold rolling microstructure, is easy to be formed uneven
Even tissue has a significant impact the toughness indexs such as elongation percentage, forming property is caused to reduce, and soaking time is long, is easy to be formed
Coarse tissue and coarse precipitates, and surface is easy to form peroxidating and surface quality is caused to decline, therefore the present invention 500~800
DEG C 30~200s of soaking time.
Cooling velocity after annealing is less than 15 DEG C/s, is easy to form pearlite in steel, steel strength is caused to reduce, therefore this
Cooling velocity >=15 DEG C of invention/s.
The present invention controls dew point -20~-50 DEG C in annealing furnace, hydrogen content H in stove21~10%, dew point is too high to be easy
It causes external oxidation and decarburization serious, so that galvanizing production the surface defects such as plating leakage is occurred, and product strength is made to decline, and dew point is too low
It is too high to capacity of equipment requirement, it is difficult to realize in conventional producing line.H2The too low external oxidation for also be easy to causeing belt steel surface of content, and
Too high increase cost, therefore annealing furnace H of the present invention21~10%.Residual oxygen content is too high, is easy to cause surface oxidation, to apply
Surface quality after covering makes a significant impact.
The beneficial effects of the present invention are：1, the tensile strength of zinc-plated super-high strength steel provided by the invention reaches 1000MPa
More than, tensile strength >=1000MPa, yield tensile ratio >=0.70, elongation percentage A80>=15%, hole expansibility >=30%, have it is good at
Shape performance, and product surface quality is good, is suitable for manufacturing the automobile structure more demanding to corrosion resistance and household electrical appliances, building
Structural member；2, the present invention provides a kind of ingredients of the zinc-plated super-high strength steel of 1000MPa grades of suitable minimizing production procedure
And its minimizing manufacturing method, the cold rolling process of traditional processing technology flow is eliminated, production procedure is significantly shortened, production process
Energy consumption and CO2Discharge can substantially reduce, and production efficiency can be obviously improved.
Specific implementation mode
To make those skilled in the art more fully understand technical scheme of the present invention, the present invention is made with reference to embodiment
It is described in further detail.
Embodiment 1
The present embodiment provides a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, specifically follow the steps below life
Production：It smelts, → pickling → continuous annealing → zinc-plated is batched in the passage finish rolling → cooling → of the passage roughing of continuous casting → heating or soaking → 3 → 5
→ finishing → finished product.
Using converter, LF refining, RH vacuum metlings, control steel product ingredient is 0.16%C, 0.30%Si, 1.8%Mn,
0.35%V, 0.020%Als, 0.15%Mo, 0.002%P, 0.002%S, 0.003%N, 0.04%Ti carry out this strand
Then continuous casting, slab thickness 80mm carry out three passage roughing by this heating strand to 1220 DEG C, obtain the intermediate base of 15mm, slightly
1050 DEG C of finishing temperature is rolled, then roughing reduction ratio 81.3% carries out 5 passage finish rolling, 900 DEG C of finish rolling finishing temperature, product thickness
2.0mm is spent, finish rolling reduction ratio 86.6% is quickly cooled down after finish rolling, 650 DEG C or more of 25 DEG C/s of average cooling rate, volume
400 DEG C of temperature is taken, this hot-strip is subjected to pickling, then carries out annealing zinc-plated, 750 DEG C, annealing time 200s of annealing temperature,
It is cooled down after annealing, 18 DEG C/s of cooling rate, is cooled to 465 DEG C, subsequent strip enters zinc pot, 455 DEG C of zinc liquid temperature, zinc liquid aluminium
Content 0.18% after strip goes out zinc pot, carries out plating postcooling to room temperature, -30 DEG C of dew point, hydrogen content in stove when zinc-plated annealing
4.5%, residual 2~10ppm of oxygen, it is zinc-plated after strip after 0.6% finishing, obtain no surface dezincification and leak source, surface quality
Good hot-dip galvanized high-strength steel finished product.
Examine hot-dip galvanized high-strength steel finished product microstructure and mechanical property, ferrite volume fraction obtained by the present embodiment
90%, remaining is bainite, the percent by volume 0.40% of carbide particle≤10nm, tensile strength 1020MPa, yield tensile ratio
0.85, elongation percentage 16%, hole expansibility 35%.
Embodiment 2
The present embodiment provides a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, specifically follow the steps below life
Production：It smelts, → pickling → continuous annealing → zinc-plated is batched in the passage finish rolling → cooling → of the passage roughing of continuous casting → 3 → heating or soaking → 5
→ finishing → finished product.
Using converter, LF refining, RH vacuum metlings, control steel product ingredient is 0.15%C, 0.30%Si, 1.8%Mn,
0.30%V, 0.03%Als, 0.006%P, 0.001%S, 0.004%N, 0.03%Ti, 0.003%B connect this strand
This strand is carried out three passage roughing, obtains the intermediate base of 18mm, roughing reduction ratio 90%, roughing by casting, slab thickness 120mm
Then 1040 DEG C of finishing temperature carries out being heated to 1080 DEG C, then carry out 5 passage finish rolling, 900 DEG C of finish rolling finishing temperature, product
Thickness 1.6mm, roughing reduction ratio 91% are quickly cooled down after finish rolling, 650 DEG C or more of 25 DEG C/s of average cooling rate, volume
520 DEG C of temperature is taken, this hot-strip is subjected to pickling, then carries out annealing zinc-plated, 820 DEG C, annealing time 100s of annealing temperature,
It is cooled down after annealing, 20 DEG C/s of cooling rate, is cooled to 470 DEG C, subsequent strip enters zinc pot and carries out zinc-plated, zinc liquid temperature 455
DEG C, zinc liquid aluminium content 0.21% after strip goes out zinc pot, carries out plating postcooling to room temperature, -45 DEG C of dew point in stove when zinc-plated annealing,
Hydrogen content 3%, residual 2~10ppm of oxygen, it is zinc-plated after strip after 0.5% finishing, obtain no surface dezincification and leak source, table
The second best in quality finished product in face.
Examine hot-dip galvanized high-strength steel finished product microstructure and mechanical property, ferrite volume fraction obtained by the present embodiment
The percent by volume 0.530% of 90%, carbide particle≤10nm, remaining is martensitic structure, product tensile strength
1150MPa, yield tensile ratio 0.82, elongation percentage 21%, hole expansibility 45%.
Embodiment 3
The present embodiment provides a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, specifically follow the steps below life
Production：Smelt, the passage finish rolling → cooling → of continuous casting → heating or soaking → 7 batch → pickling → continuous annealing → zinc-plated → finishing → at
Product.
Using converter, LF refining, RH vacuum metlings, control steel product ingredient is 0.06%C, 0.50%Si, 2.2%Mn,
0.39%V, 0.010Nb%, 0.02%Als, 0.002%P, 0.002%S, 0.30%Cr, 0.002%N, 0.003%B, by this
Strand carries out continuous casting, and slab thickness 56mm, by this heating strand, then 1220 DEG C of tapping temperature carries out 7 passage finish rolling, finish rolling
860 DEG C of finishing temperature obtains 1.2mm finished products, and finish rolling reduction ratio 97.8% is quickly cooled down after finish rolling, 650 DEG C or more flat
This hot-strip is carried out pickling, then carries out zinc-plated, annealing temperature of annealing by 45 DEG C/s of equal cooling rate, 400 DEG C of coiling temperature
795 DEG C, annealing time 120s is cooled down after annealing, 30 DEG C/s of cooling rate, is cooled to 460 DEG C, subsequent strip enter zinc pot into
Row zinc-plated, 455 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.18%, after strip goes out zinc pot, carry out plating postcooling to room temperature, it is zinc-plated to move back
- 25 DEG C of dew point in stove when fiery, hydrogen content 4%, residual 2~10ppm of oxygen, it is zinc-plated after strip after 0.6% finishing, obtain nothing
Surface dezincification and the good finished product of leak source, surface quality.
Examine hot-dip galvanized high-strength steel finished product microstructure and mechanical property, ferrite volume fraction obtained by the present embodiment
The percent by volume 1.00% of 95%, carbide particle≤10nm, remaining is martensite, product tensile strength 1060MPa, Qu Qiang
Than 0.82, elongation percentage 21%, hole expansibility 50%.
Embodiment 4
The present embodiment provides a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, specifically follow the steps below life
Production：Smelt, the passage finish rolling → cooling → of continuous casting → heating or soaking → 7 batch → pickling → continuous annealing → zinc-plated → finishing → at
Product.
Using converter, LF refining, RH vacuum metlings, control steel product ingredient is 0.09%C, 0.50%Si, 2.30%Mn,
0.35%V, 0.010Nb%, 0.02%Als, 0.002%P, 0.002%S, 0.20%Cr, 0.002%N, 0.0025%B, will
This strand carries out continuous casting, and slab thickness 56mm, by this heating strand, then 1220 DEG C of tapping temperature carries out 7 passage finish rolling, essence
860 DEG C of finishing temperature is rolled, 1.2mm finished products are obtained, finish rolling reduction ratio 97.8% is quickly cooled down after finish rolling, 650 DEG C or more
This hot-strip is carried out pickling, then carries out annealing zinc-plated by 45 DEG C/s of average cooling rate, 400 DEG C of coiling temperature, annealing temperature
765 DEG C of degree, annealing time 120s is cooled down after annealing, and 30 DEG C/s of cooling rate is cooled to 460 DEG C, and subsequent strip enters zinc pot
Zinc-plated, 455 DEG C of zinc liquid temperature is carried out, zinc liquid aluminium content 0.18% after strip goes out zinc pot, carries out heating heat treatment, heat treatment temperature
550 DEG C of degree carries out plating postcooling to room temperature after heat treatment, plate postcooling 10 DEG C/s of rate, dew point -25 in stove when zinc-plated annealing
DEG C, hydrogen content 4%, residual 2~10ppm of oxygen, it is zinc-plated after strip after 0.4% finishing, obtain no surface dezincification and leak source,
The good finished product of surface quality.
Examine hot-dip galvanized high-strength steel finished product microstructure and mechanical property, ferrite volume fraction obtained by the present embodiment
The percent by volume 0.70% of 92%, carbide particle≤10nm, remaining is bainite and martensite, product tensile strength
1030MPa, yield tensile ratio 0.76, elongation percentage 22%, hole expansibility 55%.
Claims (6)
1. a kind of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels, which is characterized in that the hot-dip galvanized high-strength steel includes following
The chemical composition of weight percent：C：0.06~0.18%, Mn：1.60~2.50%, Als：0.005~0.050%, Si：
0.10~0.50%, V：0.20~0.40%, P：≤ 0.015%, S：≤ 0.010%, N：≤ 0.008%, remaining is for Fe and not
Evitable impurity, product microstructure is mainly by 85~95% ferrites, 0~10% bainite, 0~10% martensite group
At, and in steel≤the precipitate percent by volume of 10nm is 0.2~1%.
2. tensile strength 1000MPa grades of hot-dip galvanized high-strength steels according to claim 1, which is characterized in that it is described chemistry at
It further includes at least one of Nb, Ti, Cr, Mo, B element to divide, and mass percent is shared by each element：Nb：0.005~
0.050%, Ti：0.005~0.15%, Cr：0.05~0.30%, Mo：0.05~0.50%, B：0.0005~0.003%.
3. a kind of minimizing manufacturer of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels according to claim 1 or 2
Method, which is characterized in that specifically include following steps：Steel-making, refining, continuous casting hot rolling, pickling, zinc-plated, finishing of annealing；
The continuous casting hot-rolled step is：Continuous casting, heating, roughing, finish rolling is cooling, batches, and wherein heating temperature is 1150~1300
DEG C, roughing temperature is 900~1300 DEG C, roughing reduction ratio >=80%, and final rolling temperature is 850~950 DEG C, finish rolling reduction ratio >=
70%, in cooling procedure at 650 DEG C or more, average cooling rate >=20 DEG C/s is batched in 200~600 DEG C of completions；Or
The continuous casting hot-rolled step is：Continuous casting, roughing, heating, finish rolling is cooling, batches, and wherein roughing temperature is 900 DEG C or more,
Then roughed bloom is heated to 900~1200 DEG C by roughing reduction ratio >=80%, finish rolling, finish rolling pressure are completed at 850~950 DEG C
Rate >=70%, in cooling procedure at 650 DEG C or more, average cooling rate >=20 DEG C/s is batched in 200~600 DEG C of completions；Or
The continuous casting hot-rolled step is：Continuous casting, heating, finish rolling is cooling, batches, and wherein heating temperature is 1150~1300 DEG C,
850~950 DEG C of completion finish rolling, finish rolling reduction ratio >=90%, in cooling procedure at 650 DEG C or more, average cooling rate >=20
DEG C/s, it is batched in 200~600 DEG C of completions.
4. the minimizing manufacturing method of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels according to claim 3, feature
Be, the zinc-plated step of the annealing include strip heating, soaking, cooling, it is zinc-plated, plate postcooling, wherein soaking temperature 550~
840 DEG C, 30~200s of soaking time, cooling rate >=15 DEG C/s in cooling procedure, strip enters zinc pot temperature 440 in galvanizing process
~500 DEG C, 450~470 DEG C of zinc liquid temperature, zinc liquid aluminium content 0.15~0.25%, dew point -20~-50 DEG C in annealing furnace, in stove
Hydrogen content is 1~10%, residual oxygen≤30ppm.
5. the minimizing manufacturing method of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels according to claim 3, feature
It is, the zinc-plated step of annealing includes strip heating, soaking, cooling, zinc-plated, plating postcooling, heat treatment, plates postcooling,
550~840 DEG C, 30~200s of soaking time of middle soaking temperature, soaking to zinc-plated cooling rate >=15 DEG C/s, in galvanizing process
Strip enters 440~500 DEG C of zinc pot temperature, 450~470 DEG C of zinc liquid temperature, and 500~600 DEG C of heat treatment temperature plates postcooling rate
>=8 DEG C/s, zinc liquid aluminium content 0.15~0.25%, dew point -20~-50 DEG C in annealing furnace, hydrogen content is 1~10% in stove,
Residual oxygen≤30ppm.
6. the minimizing manufacturing method of tensile strength 1000MPa grades of hot-dip galvanized high-strength steels according to claim 3, feature
It is, the finishing step finishing reduction ratio 0.1~1%.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109504930A (en) * | 2018-12-20 | 2019-03-22 | 唐山钢铁集团有限责任公司 | Tensile strength is greater than the hot-dip galvanizing sheet steel and its production method of 1300MPa |
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101270439A (en) * | 2007-03-23 | 2008-09-24 | 宝山钢铁股份有限公司 | High-strength hot-rolled armor plate and method for manufacturing same |
| CN101649415A (en) * | 2008-08-12 | 2010-02-17 | 株式会社神户制钢所 | High-strength steel sheet superior in formability |
| KR20140002272A (en) * | 2012-06-28 | 2014-01-08 | 현대제철 주식회사 | Quenched and galvanized steel sheet and method of manufacturing steel product using the same |
| CN104561775A (en) * | 2013-10-10 | 2015-04-29 | 鞍钢股份有限公司 | An economical type high-strength hot-rolled-substrate galvanized sheet and a manufacturing method thereof |
| KR20150075564A (en) * | 2013-12-26 | 2015-07-06 | 주식회사 포스코 | Zn PLATED STEEL SHEET HAVING EXCELLENT SURFACE QUALITY AND DELAYED FRACTURE RESISTANCE AND METHOD FOR MANUFACTURING THE SAME |
| CN104968819A (en) * | 2013-01-31 | 2015-10-07 | 杰富意钢铁株式会社 | High-strength hot-rolled steel sheet and production method thereof |
| JP6007882B2 (en) * | 2013-10-15 | 2016-10-19 | 新日鐵住金株式会社 | High-strength steel sheet, high-strength hot-dip galvanized steel sheet, and high-strength alloyed hot-dip galvanized steel sheet having a maximum tensile strength of 780 MPa and excellent impact characteristics |
| CN106636911A (en) * | 2017-03-17 | 2017-05-10 | 武汉科技大学 | 900MPa hot rolling sheet steel formed by directly rolling sheet billets and manufacturing method thereof |
| CN106929771A (en) * | 2017-03-01 | 2017-07-07 | 唐山钢铁集团有限责任公司 | The 1000MPa grades of high-strength galvanized steel of two-phase and steel plate and preparation method |
-
2018
- 2018-06-28 CN CN201810684785.7A patent/CN108796375B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101270439A (en) * | 2007-03-23 | 2008-09-24 | 宝山钢铁股份有限公司 | High-strength hot-rolled armor plate and method for manufacturing same |
| CN101649415A (en) * | 2008-08-12 | 2010-02-17 | 株式会社神户制钢所 | High-strength steel sheet superior in formability |
| KR20140002272A (en) * | 2012-06-28 | 2014-01-08 | 현대제철 주식회사 | Quenched and galvanized steel sheet and method of manufacturing steel product using the same |
| CN104968819A (en) * | 2013-01-31 | 2015-10-07 | 杰富意钢铁株式会社 | High-strength hot-rolled steel sheet and production method thereof |
| CN104561775A (en) * | 2013-10-10 | 2015-04-29 | 鞍钢股份有限公司 | An economical type high-strength hot-rolled-substrate galvanized sheet and a manufacturing method thereof |
| JP6007882B2 (en) * | 2013-10-15 | 2016-10-19 | 新日鐵住金株式会社 | High-strength steel sheet, high-strength hot-dip galvanized steel sheet, and high-strength alloyed hot-dip galvanized steel sheet having a maximum tensile strength of 780 MPa and excellent impact characteristics |
| KR20150075564A (en) * | 2013-12-26 | 2015-07-06 | 주식회사 포스코 | Zn PLATED STEEL SHEET HAVING EXCELLENT SURFACE QUALITY AND DELAYED FRACTURE RESISTANCE AND METHOD FOR MANUFACTURING THE SAME |
| CN106929771A (en) * | 2017-03-01 | 2017-07-07 | 唐山钢铁集团有限责任公司 | The 1000MPa grades of high-strength galvanized steel of two-phase and steel plate and preparation method |
| CN106636911A (en) * | 2017-03-17 | 2017-05-10 | 武汉科技大学 | 900MPa hot rolling sheet steel formed by directly rolling sheet billets and manufacturing method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 唐慧: "超高强钢板技术发展动向及展望", 《世界金属导报》 * |
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