CN105925905B - 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems and its production method - Google Patents
780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems and its 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
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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
- 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
- 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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- 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
- C21D2211/008—Martensite
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Abstract
The invention discloses a kind of 780MPa grades of hot-rolled dual-phase steels of Nb Ti systems, the chemical component weight percentage of the steel is as follows：C：0.06~0.09%, Si：0~0.20%, Mn：1.30~1.60%, P：0~0.015%, S：0~0.004%, Als：0.020~0.060%, Nb：0.030~0.040%, Ti：0.025~0.045%, remaining is Fe and inevitable impurity；The cooling step of the production method of the steel uses the cold technique of three-stage control：It is 130~180 DEG C/s to control first segment cooling velocity, is cooled to 610~740 DEG C, control second segment cooling velocity is 3~8 DEG C/s, it is cooled to 590~720 DEG C, it is 50~70 DEG C/s to control third section cooling velocity, is cooled to 50~150 DEG C, and it is 10~25 DEG C to control cooler-water temperature.780MPa grades of hot-rolled dual-phase steels of tensile strength that the present invention is produced can effectively obtain ferrite+martensite duplex structure, and for the lower yield strength of steel plate up to 380~635MPa, tensile strength >=780MPa, elongation percentage can reach A50mm>=16%, 180 ° of cross bending test D=1.5a are qualified, and yield tensile ratio≤0.60, product has the characteristics of high intensity and low yield strength ratio.
Description
Technical field
The present invention relates to metallurgical technology, in particular to a kind of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel and its production method.
Background technology
With the development that automotive light weight technology works, the demand of high-strength hot-rolled automobile steel constantly expands.Institutional framework
Hot-rolled dual-phase steel for ferrite+martensite is shouldered due to having the characteristics that high intensity, low yield strength ratio in automotive wheel, insurance
Gradually replace general-utility car structural steel on part, application amount gradually increases.
Because of hot-rolled dual-phase steel function admirable, in this regard, domestic each steel mill is in the research work for carrying out related fields.Each steel mill
Equipment, technology, raw material etc. are irregular, and alloying element type, dosage, technique are all not quite similar used in production process, existing
Some hot-rolled dual-phase steels are under the premise of corresponding mechanical property requirements are met, it is difficult to take into account high intensity, low yield strength ratio and cold forming
Performance.Such as：Chinese Patent Application No. CN201210411202 disclose a kind of tensile strength 780MPa grades of hot rolling biphase plates and
Its manufacturing method, the steel plate ingredient are：C：0.07%~0.12%, Si：0.2%~0.7%, Mn：1.0%~1.8%, Als：
0.02%~0.08%, Cr：0.5%~1.2%, Nb：0.02%~0.05%, Ti：0.01%~0.03%, P<0.02%th, S
<0.005%, surplus Fe；The main points of the steel sheet manufacturing method are：The continuous casting steel billet of 80~230mm thickness is heated to 1220 ±
20 DEG C, keep the temperature 2~4 hours；It is rolled using two-stage control, 1050 DEG C of recrystallization zone rolling start rolling temperature ＞, Unhydrated cement
840~920 DEG C of finishing temperature, 2.5~6mm of finished product thickness；Finish to gauge section cooling, 20~40 DEG C/s of cooling rate, coiling temperature 500~
600℃.Coiling temperature is excessively high in process of production for above-mentioned hot rolling biphase plate, from metallographic structure change law, can not obtain
To martensitic structure, it is impossible to meet requirement of the automobile steel to high intensity, low yield strength ratio and good cold forming capability.
Invention content
Present invention aim to provide a kind of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel and its production method, the heat
Roll that two-phase hardness of steel is high, yield tensile ratio is low, cold forming capability is excellent.
To achieve the above object, the technical solution adopted by the present invention is：A kind of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel,
The chemical component weight percentage of the steel is as follows：C：0.06~0.09%, Si：0~0.20%, Mn：1.30~1.60%, P：0
~0.015%, S：0~0.004%, Als：0.020~0.060%, Nb：0.030~0.040%, Ti：0.025~
0.045%, remaining is Fe and inevitable impurity.
Further, the chemical component weight percentage of the steel is as follows：C：0.06~0.09%, Si：0.10~0.13%,
Mn：1.30~1.60%, P：0.011~0.012%, S：0.003~0.004%, Als：0.037~0.039%, Nb：0.030
~0.040%, Ti：0.025~0.045%, remaining is Fe and inevitable impurity.
A kind of production method of above-mentioned Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel including smelting, vacuum processing, continuous casting, adds
Heat, the step of rolling, cool down and batching, the cooling step use the cold technique of three-stage control：Control first segment cooling velocity be
130~180 DEG C/s, 610~740 DEG C are cooled to, control second segment cooling velocity is 3~8 DEG C/s, is cooled to 590~720 DEG C,
It is 50~70 DEG C/s to control third section cooling velocity, is cooled to 50~150 DEG C, and it is 10~25 DEG C to control cooler-water temperature.
Further, the milling step is rolled using segmentation, and control roughing end temp is 1080~1120 DEG C, control
Finish rolling finishing temperature is 870~910 DEG C.
Further, the heating stepses, control slab heating temperature are 1260~1320 DEG C, heating time for 60~
70min。
Further, the cooling step, control first segment cooling velocity is 165~180 DEG C/s, is cooled to 610~690
DEG C, control second segment cooling velocity is 3~5 DEG C/s, is cooled to 590~630 DEG C, control third section cooling velocity is 50~65
DEG C/s, it is cooled to 90~100 DEG C.
Further, described to batch step, control coiling temperature is 50~150 DEG C.
Further, the vacuum processing step, control vacuum processing time ＞ 15min.
Further, the milling step, control roughing end temp are 1115~1120 DEG C, control finish rolling finishing temperature
It is 905~910 DEG C.
Further, the heating stepses, control slab heating temperature are 1290~1320 DEG C, heating time for 60~
70min。
The chemical composition with regard to the present invention and production method carry out analytic explanation below：
(1) chemical composition
Carbon：Carbon is cheap solution strengthening element, according to the application range of this steel grade, is mainly used for processing automotive wheel etc.
Part needs to carry out largely Pressing Deformation and processes, therefore it is required that material while intensity requirement is met, has well
Cold formability energy, if its content be less than 0.06%, the requirement of the strength of materials cannot be met, if its content is more than
0.09%, then it cannot meet the favorable forming property of material.Therefore, carbon content is limited to 0.06~0.09%.
Silicon：Silicon is cheap and effective deoxygenation of liquid steel element, while promotes ferritic formation, but excessive silicone content meeting
Deteriorate the surface quality of hot rolled steel plate, therefore stringent control has been carried out for silicone content, its content is limited to less than 0.20%.
Manganese：Manganese is to improve intensity and the most effective element of toughness, perlitic transformation can be effectively postponed in dual phase steel, such as
Its content of fruit is less than 1.30%, then cannot meet the strength of materials and require, but the manganese of excessive addition, can inhibit iron in dual phase steel
The precipitation of ferritic, in consideration of it, 1.60% will be defined to thereon.Therefore, manganese content is limited to 1.30~1.60%.
Phosphorus：In order to avoid the welding performance of material, stamping formabilily, toughness, suitability for secondary processing deteriorate, setting
Its upper content limit is 0.015%.Therefore, by phosphorus content control within 0.015%.
Sulphur：Sulphur is very harmful element.Sulphur in steel often exists with the oxide morphology of manganese, this sulphide inculsion pair
The impact flexibility of steel is anisotropy that is very unfavorable, and causing performance, therefore, sulfur content in steel need to be controlled more low more
It is good.Therefore, by sulfur content control in steel below 0.004%.
Aluminium：Aluminium adds for deoxidation, when Als contents are less than 0.020%, it is impossible to play its effect, the opposing party
Face, since the aluminium of addition volume easily forms aluminium oxide agglomerate, so, it is specified that the Als upper limits are 0.060%.Therefore, Als contents
It is limited to 0.020~0.060%.
Niobium：Niobium mainly improves the intensity of steel by crystal grain thinning and precipitation hardening, is strong carbon, nitrogen compound
Formation element mainly exists in the form of Nb (C, N) in steel, prevents growing up for austenite grain, finally make ferrite crystal grain ruler
It is very little to become smaller, thinning microstructure, when its content is less than 0.030%, it is impossible to meet the requirement of material high intensity, and the niobium added in is higher than
When 0.040%, the requirement of its intensity and processability can be met, if adding again, cost of alloy can significantly rise.So root
According to the performance objective requirement of steel grade, its content is limited to 0.030~0.040%.
Titanium：Titanium crystal grain thinning and can improve the strength and toughness of steel, and, the titanium nitride that in steel generates advantageous to welding performance
Effect is prevented to the AUSTENITE GRAIN COARSENING generated during weld heating, when its content is less than 0.025%, it is impossible to play enough
It strengthens effect, and intensity requirement is not achieved；It on the other hand, then can be due to the superfluous carbon of generation when the titanium of addition is more than 0.045%
Change titanium and toughness is caused to deteriorate, according to mechanical property target call, Ti content is limited to 0.025~0.045%.
Other than the range to more than chemical composition has been made to limit, go out from the viewpoint for improving formability of materials, economy
Hair, the present invention are not added with the expensive alloying elements such as Cu, Cr, Ni, Mo.
(2) production method
The present invention carries out slab heating temperature and time in the production process of 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems
Control, takes 1260~1320 DEG C of heating temperatures and the heating time of 60~70min, to ensure that the alloying element in steel billet is complete
Dissolving.
The present invention carries out segmentation rolling, and controls roughing end temp at 1080~1120 DEG C, controls finish rolling finishing temperature
At 870~910 DEG C, if this is because roughing end temp can not ensure that finish rolling finishing temperature reaches and set less than 1080 DEG C
Definite value increases rolling load, increases energy consumption, such as higher than 1120 DEG C, then can generate more iron scale, influence the surface of steel
Quality；If finish rolling finishing temperature is less than 870 DEG C, the defects of can be rolled in the two-phase region of material, cause mixed crystal, such as
Finish rolling finishing temperature is higher than 910 DEG C, then the original austenite grains of steel can be excessively coarse, reduces the intensity of steel.
For the present invention using three-stage Controlled cooling process, first segment cooling velocity is 130~180 DEG C/s, it is cooled to 610~
740 DEG C, second segment cooling velocity is 3~8 DEG C/s, is cooled to 590~720 DEG C, third section cooling velocity is 50~70 DEG C/s, cold
But it is the key technology of the present invention to 50~150 DEG C/s, first segment cooling procedure is 130~180 according to cooling velocity first
DEG C/s carries out front end and is quickly cooled down, and is cooled to temperature as 610~740 DEG C, be in order to ensure steel recrystal grain also not
It is cooled down in time when starting to grow up, avoids the generation of coarse tissue, material is made to obtain tiny original austenite grains tissue；
Second segment cooling procedure is cooled down according to cooling velocity for 3~8 DEG C/sec, is cooled to 590~720 DEG C so that partial austenitic
Structural transformation is ferrite；Third section cooling procedure cooling velocity is 50~70 DEG C/s, is cooled to 50~150 DEG C/s so that
The austenite structure fast transition that does not change is martensitic structure when second segment cools down, so as to make steel finally obtain ferrite+
The duplex structure of martensite.
Present invention control cooler-water temperature is to ensure cooling velocity during each section of cooling at 10~25 DEG C.
Compared with prior art, the present invention has the following advantages：
780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems that the present invention is produced can effectively obtain ferrite+martensite two-phase group
It knits, the lower yield strength of steel plate is up to 380~635MPa, tensile strength >=780MPa, elongation percentage A50mm>=16%, 180 ° of transverse directions are curved
Song experiment D=1.5a is qualified, and yield tensile ratio≤0.60, product has the characteristics of high intensity and low yield strength ratio.
Description of the drawings
Fig. 1 is the metallurgical structure figure of 1 light plate of embodiment.
Specific embodiment
With reference to specific embodiments and the drawings, the present invention is described in further detail, convenient for more clearly understanding this
Invention, but they do not form the present invention and limit.
Examples 1 to 8
The production stage of 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems in Examples 1 to 8 is as follows：
1) converter smelting is carried out；
2) vacuum processing, processing time ＞ 15min；
3) be casting continuously to form base and to heating strand, slab heating temperature control at 1260~1320 DEG C, heating time 60~
70min；
4) segmentation rolling is carried out：Roughing end temp is controlled at 1080~1120 DEG C, control finish rolling finishing temperature 870~
910℃；
5) using three-stage Controlled cooling process：First segment cooling velocity is 130~180 DEG C/s, is cooled to 610~740
DEG C, second segment cooling velocity is 3~8 DEG C/s, is cooled to 590~720 DEG C, third section cooling velocity is 50~70 DEG C/s, is cooled down
To 50~150 DEG C/s, control cooler-water temperature is at 10~25 DEG C；
6) it is batched, control coiling temperature is at 50~150 DEG C；
7) finishing and rear process are carried out.
The chemical composition of each Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel and its weight percent see the table below in Examples 1 to 8
1。
Main technologic parameters in Examples 1 to 8 involved in each Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel production process are shown in
The following table 2.
The mechanical property of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel obtained and histological test result are shown in Examples 1 to 8
The following table 3.
The metallurgical structure of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel obtained is shown in Fig. 1 in embodiment 1.
Comparative example 1~2
The production stage of steel grade and Examples 1 to 8 are cold difference lies in three-stage is not used to control in comparative example 1~2
But technique, the whole cooling velocity with 25 DEG C/s cool down.
The chemical composition of steel and its weight percent see the table below 1 in comparative example 1~2.
The main technologic parameters that steel is related in process of production in comparative example 1~2 see the table below 2.
The mechanical property of steel obtained and histological test result see the table below 3 in comparative example 1~2.
Table 1
Table 2
Table 3
More than the lower yield strength 413MPa of steel that obtains of the present invention is can be seen that from 1~3 data of table, tensile strength >=
793MPa, elongation percentage A50mm>=18%, 180 ° of cross bending test D=1.5a are qualified, yield tensile ratio≤0.60, have high intensity and
The characteristics of low yield strength ratio, and the yield tensile ratio ＞ 0.60 for the steel that comparative example 1~2 is obtained, the characteristics of without low yield strength ratio.Implement
Fig. 1 is shown in the metallographic structure of steel made from example 1, is the duplex structure of ferrite and martensite, and crystal grain is fine and closely woven uniformly.
Claims (8)
1. a kind of Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel, it is characterised in that：The chemical component weight percentage of the steel is as follows：
C：0.06~0.09%, Si：0~0.20%, Mn：1.30~1.60%, P：0~0.015%, S：0~0.004%, Als：
0.020~0.060%, Nb：0.030~0.040%, Ti：0.025~0.045%, remaining is Fe and inevitable impurity；
The production method of the steel, including smelting, vacuum processing, continuous casting, heating, rolling, cool down and batch the step of, the cooling step
Using the cold technique of three-stage control：It is 165~180 DEG C/s to control first segment cooling velocity, is cooled to 610~690 DEG C, control second
Section cooling velocity is 3~5 DEG C/s, is cooled to 590~630 DEG C, control third section cooling velocity is 50~65 DEG C/s, is cooled to 90
~100 DEG C, and it is 10~25 DEG C to control cooler-water temperature.
2. Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel according to claim 1, it is characterised in that：The chemical composition of the steel
Weight percent is as follows：C：0.06~0.09%, Si：0.10~0.13%, Mn：1.30~1.60%, P：0.011~
0.012%, S：0.003~0.004%, Als：0.037~0.039%, Nb：0.030~0.040%, Ti：0.025~
0.045%, remaining is Fe and inevitable impurity.
3. the production method of 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems described in a kind of claim 1, including smelting, vacuum processing,
Continuous casting, heating, rolling, the step of cooling down and batching, it is characterised in that：The cooling step uses the cold technique of three-stage control：Control
First segment cooling velocity processed is 165~180 DEG C/s, is cooled to 610~690 DEG C, and control second segment cooling velocity is 3~5 DEG C/s,
590~630 DEG C are cooled to, control third section cooling velocity is 50~65 DEG C/s, is cooled to 90~100 DEG C, and control cooling water
Water temperature is 10~25 DEG C；The milling step is rolled using segmentation, and control roughing end temp is 1080~1120 DEG C, control essence
It is 870~910 DEG C to roll finishing temperature.
4. the production method of 780MPa grades of hot-rolled dual-phase steels of Nb-Ti systems according to claim 3, it is characterised in that：It is described to add
Hot step, control slab heating temperature are 1260~1320 DEG C, and heating time is 60~70min.
5. according to the production method of the Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel of claim 3 or 4, it is characterised in that：It is described
Step is batched, control coiling temperature is 50~150 DEG C.
6. according to the production method of the Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel of claim 3 or 4, it is characterised in that：It is described
Vacuum processing step, control vacuum processing time ＞ 15min.
7. according to the production method of the Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel of claim 3 or 4, it is characterised in that：It is described
Milling step, control roughing end temp are 1115~1120 DEG C, and control finish rolling finishing temperature is 905~910 DEG C.
8. according to the production method of the Nb-Ti systems 780MPa grades of hot-rolled dual-phase steel of claim 3 or 4, it is characterised in that：It is described
Heating stepses, control slab heating temperature are 1290~1320 DEG C, and heating time is 60~70min.
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| CN111218620B (en) * | 2018-11-23 | 2021-10-22 | 宝山钢铁股份有限公司 | High-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof |
| CN113737086A (en) * | 2020-05-27 | 2021-12-03 | 宝山钢铁股份有限公司 | Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof |
| CN112680654A (en) * | 2020-11-18 | 2021-04-20 | 邯郸钢铁集团有限责任公司 | 500 MPa-grade high-strength hot-rolling acid-pickling substrate and production method thereof |
| CN117660831A (en) * | 2022-08-23 | 2024-03-08 | 宝山钢铁股份有限公司 | Dual-phase steel and manufacturing method thereof |
| CN115537675B (en) * | 2022-09-15 | 2023-09-26 | 武汉钢铁有限公司 | 800 MPa-level surface-treatment-free commercial vehicle steel and production method thereof |
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| CN101880825B (en) * | 2010-07-08 | 2012-03-14 | 东北大学 | Ultrafine grained hot rolled dual-phase steel with tensile strength of above 750MPa and manufacturing method of plate thereof |
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