CN103510008B - A kind of hot-rolled ferrite-bainite High Strength Steel Plate and manufacture method thereof - Google Patents
A kind of hot-rolled ferrite-bainite High Strength Steel Plate and manufacture method thereof Download PDFInfo
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Abstract
The present invention relates to a kind of hot-rolled ferrite-bainite High Strength Steel Plate and manufacture method thereof, its main chemical compositions by mass percent is: C0.05 ~ 0.10%, Si0.20 ~ 0.50%, Mn0.80 ~ 1.30%, Alt0.02 ~ 0.06%, Cr0.40 ~ 0.8%, P≤0.09%, S≤0.010%, and N≤0.006% surplus is Fe and inevitable impurity; Its manufacture craft comprises hot metal pretreatment, converter smelting, alloy fine setting Argon, LF refining, continuous casting heating process, rolling technology, process for cooling and coiling technique, the present invention is on the basis of C-Mn composition of steel, strict control C and Mn content, reduce Si content, appropriate interpolation Cr and P, do not add Nb, V, Ti microalloy element, also the precious alloys such as Mo, Ni are not added, significantly reduce cost, adopt suitable cooling controlling and rolling controlling process, obtain the hot-rolled ferrite-bainite dual-phase steel that tensile strength reaches 550 ~ 650MPa level, hole expansibility is high, and forming property is excellent.
Description
Technical field
The invention belongs to ferrous materials engineering field, particularly a kind of low cost hot-rolled ferrite-bainite High Strength Steel Plate and manufacture method thereof.
Background technology
In recent years, along with the fast development of modern automobile industry, energy day is becoming tight, environmental stress increasingly sharpens, and adds constantly perfect to legislative work for protecting environment of the whole world, facilitates automotive technology development center of gravity towards energy-saving and environmental protection and the development of security aspect.Automobile lightweight, reduction fuel oil consumption, increase weight-carrying capacity, raising conveying efficiency become modal keyword.The auto output of ending China in 2012 has broken through 1,900 ten thousand, within continuous 4 years, keeps the status of the large automobile production state of the first in the world.Ferrous materials is the maximum key raw material of current automobile making application percentage, accounts for about 65%.Meanwhile, auto sheet also must meet the safe, energy-conservation of automobile and low emission, the item requirement such as attractive in appearance, anticorrosion.In order to alleviate car weight, reduce oil consumption, emissions reduction and raising security, automotive sheet becomes inexorable trend to high strength development.
Hot-rolled high-strength steel plate, for making the automobile traveling such as chassis and wheel parts, is one of the most effective most important approach realizing car body loss of weight.Automotive chassis components does not expose, very strict to the surface quality requirements of steel plate, but complex-shaped due to it, main forming mode comprises: stretch flanging, bending, reaming and spark-erosion sinking etc., these forming modes are to the plasticity of steel plate, and especially Extending flange Perfor requires higher.The widely different two-phase of deformability (ferrite+martensite) interface is there is in traditional ferrite/martensite two-phase (FMDP) steel, easily at perforate position cracking in forming process, be unfavorable for the shaping of the component such as the automobile traveling of requirement high hole expandability and suspension.And ferrite/bainite dual phase steel also claims high reaming steel, compared with the FMDP steel of same intensity rank, FBDP steel has excellent breaking elongation and hole expansibility concurrently.Therefore, FBDP steel is more suitable for punching press requires higher Extending flange Perfor parts as wheel spoke, automobile chassis etc.
Publication number CN101643880A discloses a kind of high tensile strength hot rolled ferrite bainite dual phase steel and manufacture method thereof, its main chemical compositions by mass percent is: 0.05 ~ 0.15%C, 0.50 ~ 1.00%Si, 1.00 ~ 1.50%Mn, P≤0.020%, S≤0.010%, 0.03 ~ 0.05%Al, N≤0.006% surplus are Fe and inevitable impurity, this composition silicone content is high, surface quality is restive, and its tensile strength rank is >=490MPa level, intensity is lower.
Publication number CN1680613A discloses a kind of hot-rolled low carbon bainite composite diphase material and preparation technology thereof, its main chemical compositions by mass percent is: 0.03 ~ 0.12%C, 0.30 ~ 1.50%Si, 1.00 ~ 2.00%Mn, P≤0.030%, S≤0.020%, 0.0005 ~ 0.005%B, 0.006 ~ 0.06%Nb, 0.01 ~ 0.05Ti, surplus are Fe, this composition also has higher silicon, especially containing the element such as B, Nb, Ti, higher as non-recrystallization controlled rolling and total deformation >=25% etc. of last three passages to manufacture process requirement in addition.
Publication number CN103088258A discloses a kind of 590MPa level dual phase steel and production method thereof, its chemical composition is C≤0.20% preferably 0.06 ~ 0.10%, Si≤1.80%, Mn≤2.0% is preferably 1.40 ~ 1.60%, P≤0.05% is P≤0.02% preferably, S≤0.015% preferably≤0.010%, Nb≤0.10 is preferably 0.04 ~ 0.05%, Ti≤0.10% is preferably 0.010 ~ 0.025%, to be a kind of Nb microalloying be main Composition Design, cost is higher, its production method mainly adopts non-recrystallization controlled rolling also higher to milling equipment Capability Requirement, the air cooling time of sub-sectional cooling requires to be 6 ~ 11S, require higher to the length of section cooling line and cooling power, it is larger that many hot rolling lines realize difficulty.
Publication number CN101603153A discloses a kind of hot-rolled ferrite-bainite dual-phase steel and manufacture method thereof, its main chemical compositions by mass percent is: 0.06 ~ 0.08%C, 0.40 ~ 0.60%Si, 1.40 ~ 1.60%Mn, P≤0.020%, S≤0.020%, 0.40 ~ 0.60%Cr, 0.02 ~ 0.04%Nb, Fe content is higher, and containing valuable microalloy element Nb, cost is also higher, especially its manufacture method needs low temperature non-recrystallization controlled rolling (finish to gauge 800 ~ 830 DEG C) higher to equipment of hot rolling Capability Requirement, the air cooling time of sub-sectional cooling requires to be 12 ~ 15S, require too high to the length of section cooling line and cooling power, it is very large that many hot rolling lines realize difficulty.
Summary of the invention
The object of the invention is to provide a kind of low cost high formability hot-rolled ferrite-bainite high-strength steel and manufacture method thereof for above deficiency.
The present invention is achieved by the following technical solutions:
A kind of hot-rolled ferrite-bainite High Strength Steel Plate, its main chemical compositions by mass percent is: C0.05 ~ 0.10%, Si0.20 ~ 0.50%, Mn0.80 ~ 1.30%, Alt0.02 ~ 0.06%, Cr0.40 ~ 0.8%, P≤0.09%, S≤0.010%, N≤0.006%, surplus is Fe and inevitable impurity.
In above-mentioned firm plate, ferrite volume fraction is 50 ~ 80%, and bainite volume fraction is 20 ~ 50%.
The manufacture method of above-mentioned a kind of hot-rolled ferrite-bainite High Strength Steel Plate, comprises the following steps: hot metal pretreatment, converter smelting, alloy fine setting Argon, LF refining, continuous casting and hot continuous rolling.
Above-mentioned hot continuous rolling comprises heating process, rolling technology, process for cooling and coiling technique.
The manufacture method of above-mentioned a kind of hot-rolled ferrite-bainite High Strength Steel Plate, described hot continuous rolling concrete technology is:
(1) heating process: by the heating of plate blank of thickness 70 ~ 230mm to 1150 ~ 1250 DEG C, soaking time 0.5-3 hour;
(2) rolling technology: adopt two-stage control rolling, rough rolling step single pass draft >=20%, total reduction is >=70%, and finish rolling stage draft is >=75%; Rough rolling step start rolling temperature is 1100 ~ 1150 DEG C, finishing temperature 1050 ~ 1100 DEG C, and finish rolling stage start rolling temperature is 1000 ~ 1050 DEG C, and finishing temperature is 830 ~ 880 DEG C;
(3) process for cooling: the sectional type cooling path control techniques of rolling rear employing first stage water-cooled+air cooling+subordinate phase water-cooled, first stage water-cooled section speed of cooling is 20 ~ 80 DEG C/s, be cooled to 650 ~ 750 DEG C, then air cooling 2-5s, subordinate phase water-cooled section speed of cooling is 20 ~ 80 DEG C/s, is cooled to 400-500 DEG C;
(4) coiling technique: take middle warm rolling to get, coiling temperature 400-500 DEG C, finished product thickness is 2 ~ 10mm.The invention has the beneficial effects as follows: the present invention is on the basis of C-Mn composition of steel, strict control C and Mn content, reduce Si content, appropriate interpolation Cr and P, does not add Nb, V, Ti microalloy element, also the precious alloys such as Mo, Ni are not added, significantly reduce cost, adopt suitable cooling controlling and rolling controlling process, obtain the hot-rolled ferrite-bainite dual-phase steel that tensile strength reaches 550 ~ 650MPa level, hole expansibility is high, and forming property is excellent.When using steel plate of the present invention, can adapt to require the automotive wheel of high strength, high fatigue property, hang the formed machining of component and other industrial machinery part etc.
Accompanying drawing explanation
Fig. 1 is the ferrite bainite in the embodiment of the present invention 2 transmission electron microscope macrograph
Fig. 2 is the high density dislocation ferrite in the embodiment of the present invention 3 transmission electron microscope
Embodiment
The present invention is on the basis of C-Mn composition of steel, suitable adjustment C and Mn content, reduce Si content, by adding the elements such as P, Cr, do not add Nb, V, Ti microalloy element, also do not add the expensive alloying elements such as Mo, Ni, its main chemical compositions by mass percent is: 0.05 ~ 0.10%C, 0.20 ~ 0.50%Si, 0.80 ~ 1.30%Mn, 0.02 ~ 0.06%Alt, P≤0.09%, 0.40 ~ 0.80%Cr, S≤0.005%, and N≤0.006% surplus is Fe and inevitable impurity; Utilize comparatively high temps finish to gauge+cooling path control+middle warm rolling to get methods such as (400 ~ 500 DEG C), obtain the duplex structure of ferrite and bainite, thus realize the optimal performance combination of the performance index such as high strength, unit elongation and hole expansibility.
Manufacture method of the present invention comprises following three parts: 1) heating process; 2) rolling process; 3) refrigerating work procedure.In order to obtain steel plate of the present invention efficiently, be necessary the key process parameter reasonably controlling above-mentioned a few part, to ensure to obtain desirable microstructure and mechanical property.
1. heating process
Be that the continuously cast bloom of 70-230mm is heated to 1150 ~ 1250 DEG C, soaking time 0.5-3 hour by thickness.Slab reheats process main purpose and comprises abundant austenitizing and by complete for alloying element solid solution and homogenizing.
2. rolling process
Adopt two-stage control rolling, roughing total reduction >=70%, finish rolling draft >=75%; Roughing district start rolling temperature is 1100 ~ 1150 DEG C, and finish rolling district start rolling temperature is 1000 ~ 1050 DEG C, and finishing temperature is 830 ~ 880 DEG C.Roughing total reduction >=70%, and single pass draft then reaches more than 20%, mainly through sufficient Static Recrystallization significantly fining austenite grains between dynamic and passage.
Recrystallization zone controlled rolling is another main characteristics of rolling technology of the present invention.Finish rolling district temperature controls usually within the scope of 1000 ~ 850 DEG C, and the non-recrystallization temperature (Tnr) of the present invention typical case steel grade is usually below 850 DEG C, only has rear several passage due to the raising of roll speed, the shortening of rolling intermittent time and recrystallize is occurred may be insufficient, so finishing stands belongs to recrystallization temperature scope substantially.Finish rolling total reduction controls more than 75%, the deformation energy in austenite needed for recrystallize can be increased substantially, promote fully carrying out of passage recrystallize, particularly in the former passage of finish rolling, the effect playing sufficient fining austenite grains of perfect recrystallization, the then generation of the partial, re-crystallization of a few passage can improve the effect of Strain Accumulation, to obtaining ultra-fine and uniform austenite crystal and high residual strain before phase transformation.
A large amount of research work shows, fining austenite grains, and hardening strain is accumulated, and mainly plays the effect of following two aspects: a) promote the diffusion of C towards periphery in austenite, and the strong austenite that promotes is to ferritic transformation; B) rapid diffusion of C facilitate around in austenite rich C improve its stability, postpone perlitic transformation, make to generate low-carbon bainite lath in warm area cooling range in wider, transmission organizes the generation of middle plate strip bainite to absolutely prove this point (Fig. 1).Therefore, the controlled rolling of course of hot rolling is that the present invention realizes one of key link of low cost ferrite-bainite high-strength steel exploitation.
3. refrigerating work procedure
In the present invention, refrigerating work procedure mainly contains following two main points: a) sub-sectional cooling; B) in, warm rolling is got.
Sub-sectional cooling adopts the syllogic cooling path master mode of " after finish to gauge water-cooled+air cooling+back segment water-cooled ", organizational advantage, the suppression austenite reversion process of Austenite Grain Refinement after after recrystallize controlled rolling, water-cooled to ferritic transformation district (usually at 650 ~ 750 DEG C) can retain Controlled Cooling immediately, enough residual strain effects before ensureing phase transformation, thus strongly promote austenite → ferrite transformation process, significantly fining ferrite grains size while of obtaining ferritic.In addition, after finish to gauge, rapid cooling also makes the dislocation (Fig. 2) remaining some amount in newly-generated ferrite, and this raising for steel strength, extension and reaming performance has important effect.
During the usual torrid zone produces, the working temperature of reeling machine is mainly at 500 ~ 750 DEG C, the most common with about 600 DEG C.Less than 200 DEG C low temperature batch and have industrially implemented a lot of problem.The present invention makes the stability of retained austenite around ferrite greatly strengthen due to P, Cr alloying process and grain refining controlled rolling, in tissue, second-phase will obtain low-carbon bainite, thus about coiling temperature to 400 ~ 500 DEG C can be improved, alleviate the load of reeling machine to a great extent, enhance productivity.
Adopt syllogic sub-sectional cooling after finish to gauge of the present invention, first stage rate of cooling is 20 ~ 80 DEG C/s, middle air cooling 2 ~ 5s, and subordinate phase water-cooled section speed of cooling is 20 ~ 80 DEG C/s, coiling temperature 400 ~ 500 DEG C, and finished product thickness is 2 ~ 10mm.
Embodiment 1
A kind of hot-rolled ferrite-bainite high-strength steel, its chemical composition is in table 1.
A production method for hot-rolled ferrite-bainite high-strength steel, comprises hot metal pretreatment-converter smelting-alloy fine setting Argon-LF-continuous casting-hot continuous rolling.Described hot continuous rolling process is: slab thickness 135mm, Heating temperature 1180 DEG C, soaking time 2h, roughing start rolling temperature 1130 DEG C, finishing temperature 1070 DEG C, 3 passes become the intermediate blank of 33mm, finish rolling stage start rolling temperature 1020 DEG C, finishing temperature 880 DEG C, then 729 DEG C are chilled to the cooling rate of 64 DEG C/S, air cooling 3S, then with 56 DEG C/S water-cooled to target coiling temperature, coiling temperature is 496 DEG C, steel plate finished product thickness 4mm.
Embodiment 2
A kind of hot-rolled ferrite-bainite high-strength steel, its chemical composition is in table 1.
A production method for hot-rolled ferrite-bainite high-strength steel, comprises hot metal pretreatment-converter smelting-alloy fine setting Argon-LF-continuous casting-hot continuous rolling.Described hot continuous rolling process is:
Slab thickness 135mm, Heating temperature 1160 DEG C, soaking time 2.5h, roughing start rolling temperature 1110 DEG C, finishing temperature 1060 DEG C, 3 passes become the intermediate blank of 33mm, finish rolling stage start rolling temperature 1000 DEG C, finishing temperature 880 DEG C, is then chilled to 708 DEG C with the cooling rate of 58 DEG C/S, air cooling 3.5S, again with 52 DEG C/S water-cooled to target coiling temperature, coiling temperature is 462 DEG C, steel plate finished product thickness 4.5mm.
Embodiment 3
A kind of hot-rolled ferrite-bainite high-strength steel, its chemical composition is in table 1.
A production method for hot-rolled ferrite-bainite high-strength steel, comprises hot metal pretreatment-converter smelting-alloy fine setting Argon-LF-continuous casting-hot continuous rolling.Described hot continuous rolling process is: slab thickness 135mm, Heating temperature 1230 DEG C, soaking time 1.5h, roughing start rolling temperature 1140 DEG C, finishing temperature 1070 DEG C, 3 passes become the intermediate blank of 35mm, finish rolling stage start rolling temperature 1020 DEG C, finishing temperature 840 DEG C, is then chilled to 668 DEG C with the cooling rate of 37 DEG C/S, air cooling 4S, again with 28 DEG C/S water-cooled to target coiling temperature, coiling temperature is 413 DEG C, steel plate finished product thickness 6.0mm.
Embodiment 4
A kind of hot-rolled ferrite-bainite high-strength steel, its chemical composition is in table 1.
A production method for hot-rolled ferrite-bainite high-strength steel, comprises hot metal pretreatment-converter smelting-alloy fine setting Argon-LF-continuous casting-hot continuous rolling.Described hot continuous rolling process is: slab thickness 135mm, Heating temperature 1200 DEG C, soaking time 2.0h, roughing start rolling temperature 1130 DEG C, finishing temperature 1080 DEG C, 3 passes become the intermediate blank of 33mm, finish rolling stage start rolling temperature 1020 DEG C, finishing temperature 860 DEG C, is then chilled to 683 DEG C with the cooling rate of 52 DEG C/S, air cooling 3S, again with 43 DEG C/S water-cooled to target coiling temperature, coiling temperature is 437 DEG C, steel plate finished product thickness 4.5mm.
Embodiment 5
A kind of hot-rolled ferrite-bainite high-strength steel, its chemical composition is in table 1.
A production method for hot-rolled ferrite-bainite high-strength steel, comprises hot metal pretreatment-converter smelting-alloy fine setting Argon-LF-continuous casting-hot continuous rolling.Described hot continuous rolling process is: slab thickness 135mm, Heating temperature 1220 DEG C, soaking time 2.0h, roughing start rolling temperature 1140 DEG C, finishing temperature 1080 DEG C, 3 passes become the intermediate blank of 33mm, finish rolling stage start rolling temperature 1010 DEG C, finishing temperature 870 DEG C, is then chilled to 692 DEG C with the cooling rate of 72 DEG C/S, air cooling 3S, again with 56 DEG C/S water-cooled to target coiling temperature, coiling temperature is 418 DEG C, steel plate finished product thickness 4.0mm.
The chemical composition of table 1 embodiment
The mechanical property of the ferrite-bainite high-strength steel of embodiment 1 ~ 5, tissue composition and reaming performance are as shown in table 2.
The mechanical property of table 2 embodiment
Industrial production exploitativeness
As seen from the above embodiment, hot-rolled ferrite-bainite high-strength steel of the present invention and manufacture method thereof, this product and technique all can realize on most hot continuous rolling production line, large industrial production is workable, and production cost is lower, product has the feature of higher intensity and unit elongation and high hole expansibility, and mechanical property and forming property coupling are well.
Claims (1)
1. a hot-rolled ferrite-bainite High Strength Steel Plate, its main chemical compositions by mass percent is: C0.063%, Si0.33%, Mn1.26%, Alt0.041%, Cr0.66%, P0.063%, S0.003%, N0.0028%, surplus is Fe and inevitable impurity;
In described steel plate, ferrite volume fraction is 50 ~ 80%, and bainite volume fraction is 41%;
The manufacture method of above-mentioned High Strength Steel Plate, comprises the following steps: hot metal pretreatment, converter smelting, alloy fine setting Argon, LF refining, continuous casting and hot continuous rolling; Described hot continuous rolling comprises heating process, rolling technology, process for cooling and coiling technique;
Described hot continuous rolling concrete technology is:
(1) heating process: by the heating of plate blank of thickness 135mm to 1230 DEG C, soaking time 1.5 hours;
(2) rolling technology: adopt two-stage control rolling, rough rolling step single pass draft >=20%, under stagnation pressure
Rate is >=70%, and finish rolling stage draft is >=75%; Rough rolling step start rolling temperature is 1140 DEG C, finishing temperature 1070 DEG C, and 3 passes become the intermediate blank of 35mm, and finish rolling stage start rolling temperature is 1020 DEG C, and finishing temperature is 840 DEG C;
(3) process for cooling: the sectional type cooling road of rolling rear employing first stage water-cooled+air cooling+subordinate phase water-cooled
Footpath control techniques, first stage water-cooled section speed of cooling is 37 DEG C/s, is cooled to 668 DEG C,
Then air cooling 4s, subordinate phase water-cooled section speed of cooling is 28 DEG C/s, is cooled to 413 DEG C;
(4) coiling technique: take middle warm rolling to get, coiling temperature 413 DEG C, finished product thickness is 6.0mm.
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