CN105925905A - Nb-Ti-series 780MPa-class hot-rolled dual-phase steel and production method thereof - Google Patents
Nb-Ti-series 780MPa-class hot-rolled dual-phase steel and production method thereof Download PDFInfo
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- CN105925905A CN105925905A CN201610325222.XA CN201610325222A CN105925905A CN 105925905 A CN105925905 A CN 105925905A CN 201610325222 A CN201610325222 A CN 201610325222A CN 105925905 A CN105925905 A CN 105925905A
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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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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses an Nb-Ti-series 780MPa-class hot-rolled dual-phase steel. The steel comprises the following chemical components in percentages by weight: 0.06-0.09% of C, 0-0.20% of Si, 1.30-1.60% of Mn, 0-0.015% of P, 0-0.004% of S, 0.020-0.060% of Als, 0.030-0.040% of Nb, 0.025-0.045% of Ti, and the balance of Fe and inevitable impurities. In a cooling step of a production method of the steel, a three-section type controlled cooling technology is adopted and comprises the following steps: controlling the cooling speed of a first section to be 130-180 DEG C/s, and cooling until the temperature reaches 610-740 DEG C; controlling the cooling speed of a second section to be 3-8 DEG C/s, and cooling until the temperature reaches 590-720 DEG C; and controlling the cooling speed of a third section to be 50-70 DEG C/s, cooling until the temperature reaches 50-150 DEG C, and controlling the temperature of cooling water to be 10-25 DEG C. The produced hot-rolled dual-phase steel of which the tensile strength is 780 MPa class can effectively acquire ferrite+martensite dual-phase tissues effectively, the lower yield strength of a steel plate reaches 380-635 MPa, the tensile strength is greater than or equal to 780 MPa, elongation A50mm can be greater than or equal to 16%, the steel is qualified if the transverse section bend test D is equal to 1.5a, the yield-tensile ratio is less than or equal to 0.60, and the product has the features of high strength and low yield-tensile ratio.
Description
Technical field
The present invention relates to metallurgical technology, double in particular to a kind of Nb-Ti system 780MPa level hot rolling
Phase steel and production method thereof.
Background technology
Along with carrying out of automotive light weight technology work, the demand of high-strength hot-rolled automobile steel is continuous
Expand.Institutional framework is that the hot-rolled dual-phase steel of ferrite+martensite is owing to having high intensity, low
The feature of yield tensile ratio, shoulders etc. the most progressively to replace general-utility car knot on part in automotive wheel, insurance
Structure steel, application amount progressively strengthens.
Because of hot-rolled dual-phase steel function admirable, to this, domestic each steel mill is all carrying out related fields
Research work.Each steel mill equipment, technology, raw material etc. are uneven, used by production process
Alloying element kind, consumption, technique are all not quite similar, and existing hot-rolled dual-phase steel is meeting phase
On the premise of answering mechanical property requirements, it is difficult to take into account high intensity, low yield strength ratio and cold forming capability.
As: Chinese Patent Application No. CN201210411202 discloses a kind of tensile strength 780MPa
Level hot rolling biphase plate and manufacture method thereof, this steel plate composition is: 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%, S < 0.005%, surplus
For Fe；This steel sheet manufacturing method is characterized by: by 80～230mm thick continuous casting steel billet heating
To 1220 ± 20 DEG C, it is incubated 2～4 hours；Employing two-stage control rolls, and recrystallization zone rolls
Start rolling temperature ＞ processed 1050 DEG C, Unhydrated cement finishing temperature 840～920 DEG C, finished product thickness
2.5～6mm；Finish to gauge section cooling, cooling rate 20～40 DEG C/s, coiling temperature 500～600 DEG C.On
State hot rolling biphase plate coiling temperature in process of production too high, from metallographic structure change law
See, it is impossible to obtain martensitic structure, it is impossible to meet automobile steel to high intensity, low yield strength ratio and
The requirement of good cold forming capability.
Summary of the invention
Present invention aim to provide a kind of Nb-Ti system 780MPa level hot-rolled dual-phase steel and
Its production method, this hot-rolled dual-phase steel intensity is high, yield tensile ratio is low, and cold forming capability is excellent.
For achieving the above object, the technical solution used in the present invention is: a kind of Nb-Ti system
780MPa level hot-rolled dual-phase steel, the chemical component weight percentage of this 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 inevitably impurity.
Further, the chemical component weight percentage of this 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 inevitably impurity.
A kind of production method of above-mentioned Nb-Ti system 780MPa level hot-rolled dual-phase steel, including smelt,
Application of vacuum, continuous casting, the step that heats, roll, cool down and batch, described cooling step is adopted
By the cold technique of syllogic control: controlling first paragraph cooling velocity is 130～180 DEG C/s, is cooled to
610～740 DEG C, controlling second segment cooling velocity is 3～8 DEG C/s, is cooled to 590～720 DEG C, control
Making three-stage cooling speed is 50～70 DEG C/s, is cooled to 50～150 DEG C, and controls cooling water water
Temperature is 10～25 DEG C.
Further, described milling step uses segmentation rolling, controls roughing end temp and is
1080～1120 DEG C, controlling finish rolling finishing temperature is 870～910 DEG C.
Further, described heating steps, controlling slab heating temperature is 1260～1320 DEG C,
Heat time is 60～70min.
Further, described cooling step, controlling first paragraph cooling velocity is 165～180 DEG C/s,
Being cooled to 610～690 DEG C, controlling second segment cooling velocity is 3～5 DEG C/s, is cooled to 590～630
DEG C, controlling three-stage cooling speed is 50～65 DEG C/s, is cooled to 90～100 DEG C.
Further, described in batch step, controlling coiling temperature is 50～150 DEG C.
Further, described vacuum processing step, control vacuum processing time ＞ 15min.
Further, described milling step, controlling roughing end temp is 1115～1120 DEG C,
Controlling finish rolling finishing temperature is 905～910 DEG C.
Further, described heating steps, controlling slab heating temperature is 1290～1320 DEG C,
Heat time is 60～70min.
Chemical composition and production method with regard to the present invention are analyzed illustrating below:
(1) chemical composition
Carbon: carbon is cheap solution strengthening element, according to the range of application of this steel grade, mainly uses
In parts such as processing automotive wheels, need to carry out Pressing Deformation processing largely, therefore want
Ask material while meeting requirement of strength, there is good cold forming performance, if its content
Less than 0.06%, then can not meet the requirement of the strength of materials, if its content is more than 0.09%,
Then can not 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, simultaneously facilitates ferritic formation,
But too much silicone content can deteriorate the surface quality of hot rolled steel plate, therefore carries out for silicone content
Strict control, is limited to less than 0.20% by its content.
Manganese: manganese is to improve intensity and the maximally effective element of toughness, can effectively push away in dual phase steel
Perlitic transformation late, if its content is less than 1.30%, then can not meet strength of materials requirement,
But add the manganese of excess, dual phase steel can suppress ferritic precipitation, in consideration of it, by it
On be defined to 1.60%.Therefore, Fe content is limited to 1.30～1.60%.
Phosphorus: in order to avoid the welding performance of material, stamping formabilily, toughness, secondary operations
Performance deteriorates, and sets its upper content limit as 0.015%.Therefore, phosphorus content is controlled
Within 0.015%.
Sulphur: sulphur is very harmful element.Sulphur in steel often exists with the oxide morphology of manganese,
This sulphide inculsion is the most disadvantageous to the impact flexibility of steel, and causes each to different of performance
Property, therefore, need to sulfur content in steel be controlled the lowest more good.Therefore, by sulfur content control in steel
System is below 0.004%.
Aluminium: aluminium adds for deoxidation, when Als content is less than 0.020%, it is impossible to
Play its effect, on the other hand, easily form aluminum oxide agglomerate, institute owing to adding the aluminium of volume
With, it is stipulated that the Als upper limit is 0.060%.Therefore, Als content is limited to 0.020～0.060%.
Niobium: niobium mainly improves the intensity of steel by crystal grain thinning and precipitation hardening, is strong
Strong carbon, nitrogen compound form element, mainly exist with Nb (C, N) form, resistance in steel
Stopping growing up of austenite crystal, finally make ferrite grain size diminish, thinning microstructure, when it
When content is less than 0.030%, it is impossible to meet the requirement of material high intensity, and the niobium added is higher than
When 0.040%, can meet the requirement of its intensity and processability, if adding again, cost of alloy
Can significantly rise.So, according to the performance objective requirement of steel grade, its content is limited to
0.030～0.040%.
Titanium: titanium can crystal grain thinning and improve the strength and toughness of steel, and favourable to welding performance,
The titanium nitride generated in steel has preventing effectiveness to the AUSTENITE GRAIN COARSENING produced during weld heating,
When its content is less than 0.025%, it is impossible to enough play its strengthening effect, do not reach intensity and want
Ask；On the other hand, when the titanium of addition is more than 0.045%, then can be owing to generating superfluous carbonization
Titanium and cause toughness to deteriorate, according to mechanical property target call, Ti content is limited to
0.025～0.045%.
Except the scope of above chemical composition has been made limit in addition to, from improve formability of materials,
From the viewpoint of economy, the present invention is not added with the expensive alloying elements such as Cu, Cr, Ni, Mo.
(2) production method
Strand is added in the production process of Nb-Ti system 780MPa level hot-rolled dual-phase steel by the present invention
Hot temperature and time is controlled, and takes 1260～1320 DEG C of heating-up temperatures and 60～70min
Heat time, to ensure that the alloying element in steel billet is completely dissolved.
The present invention carries out segmentation rolling, and controls roughing end temp at 1080～1120 DEG C, control
Finish rolling finishing temperature processed is at 870～910 DEG C, if this is because roughing end temp is less than 1080
DEG C, then cannot ensure that finish rolling finishing temperature reaches setting value, increase rolling load, increase energy consumption,
As higher than 1120 DEG C, then can produce more iron scale, affect the surface quality of steel；
If finish rolling finishing temperature is less than 870 DEG C, then can roll in the two-phase region of material, make
Becoming the defects such as mixed crystal, if finish rolling finishing temperature is higher than 910 DEG C, then the original austenite of steel is brilliant
Grain can be the thickest, reduces the intensity of steel.
The present invention uses syllogic Controlled cooling process, first paragraph cooling velocity to be 130～180 DEG C
/ s, is cooled to 610～740 DEG C, and second segment cooling velocity is 3～8 DEG C/s, is cooled to 590～720
DEG C, three-stage cooling speed is 50～70 DEG C/s, is cooled to 50～150 DEG C/s, is the present invention
Key technology, first first paragraph cooling procedure are before 130～180 DEG C/s is carried out according to cooling velocity
End quickly cooling, being cooled to temperature is 610～740 DEG C, is to ensure that the recrystallization at steel
Crystal grain does not has started when growing up and cools down in time, it is to avoid the generation of thick tissue, makes material obtain
Obtain tiny original austenite grains tissue；Second segment cooling procedure is 3～8 according to cooling velocity
DEG C/sec cool down, be cooled to 590～720 DEG C so that partial austenitic structural transformation is iron element
Body；Three-stage cooling process cooling velocity is 50～70 DEG C/s, is cooled to 50～150 DEG C/s, makes
The austenite structure fast transition that must not change when second segment cools down is martensitic structure, thus
Steel are made finally to obtain the duplex structure of ferrite+martensite.
The present invention control cooler-water temperature 10～25 DEG C be to ensure that each section cool down time cold
But speed.
Compared with prior art, the invention have the advantages that
The Nb-Ti system 780MPa level hot-rolled dual-phase steel that the present invention is produced can effectively obtain iron element
Body+martensite duplex structure, the lower yield strength of steel plate reaches 380～635MPa, tensile strength
>=780MPa, elongation percentage A50mm>=16%, 180 ° of cross bending test D=1.5a are qualified,
Yield tensile ratio≤0.60, product possesses the feature of high intensity and low yield strength ratio.
Accompanying drawing explanation
Fig. 1 is the metallurgical structure figure of embodiment 1 light plate.
Detailed description of the invention
Below in conjunction with specific embodiments and the drawings, the present invention is described in further detail, it is simple to
More clearly understand the present invention, but they do not constitute restriction to the present invention.
Embodiment 1～8
The production stage of the Nb-Ti system 780MPa level hot-rolled dual-phase steel in embodiment 1～8 is as follows:
1) converter smelting is carried out；
2) application of vacuum, processes time ＞ 15min；
3) being casting continuously to form base and heat strand, slab heating temperature controls at 1260～1320 DEG C,
Heat time 60～70min；
4) segmentation rolling is carried out: control roughing end temp, at 1080～1120 DEG C, controls essence
Roll finishing temperature at 870～910 DEG C；
5) syllogic Controlled cooling process is used: first paragraph cooling velocity is 130～180 DEG C/s,
Being cooled to 610～740 DEG C, second segment cooling velocity is 3～8 DEG C/s, is cooled to 590～720 DEG C,
Three-stage cooling speed is 50～70 DEG C/s, is cooled to 50～150 DEG C/s, controls cooler-water temperature
At 10～25 DEG C；
6) batch, control coiling temperature at 50～150 DEG C；
7) finishing and rear operation are carried out.
In embodiment 1～8 each Nb-Ti system 780MPa level hot-rolled dual-phase steel chemical composition and
Percentage by weight see table 1.
Embodiment 1～8 relates in each Nb-Ti system 780MPa level hot-rolled dual-phase steel production process
Main technologic parameters see table 2.
The mechanical property of the Nb-Ti system 780MPa level hot-rolled dual-phase steel prepared in embodiment 1～8
And histological test result see table 3.
The metallographic structure knot of the Nb-Ti system 780MPa level hot-rolled dual-phase steel prepared in embodiment 1
Structure is shown in Fig. 1.
Comparative example 1～2
In comparative example 1～2, the production stage of steel grade is not use with the difference of embodiment 1～8
Syllogic Controlled cooling process, the omnidistance cooling velocity with 25 DEG C/s cools down.
In comparative example 1～2, chemical composition and the percentage by weight thereof of steel see table 1.
The main technologic parameters that in comparative example 1～2, steel relates in process of production see table 2.
Mechanical property and the histological test result of the steel prepared in comparative example 1～2 see table 3.
Table 1
Table 2
Table 3
From table 1～3 data it can be seen that the lower yield strength 413MPa of steel that obtains of the present invention
Above, tensile strength >=793MPa, elongation percentage A50mm>=18%, 180 ° of transverse curvature examinations
Test D=1.5a qualified, yield tensile ratio≤0.60, there is the feature of high intensity and low yield strength ratio, and
Yield tensile ratio ＞ 0.60 of the steel that comparative example 1～2 is obtained, does not have the feature of low yield strength ratio.Real
Fig. 1 is shown in the metallographic structure executing the steel that example 1 prepares, for ferrite and the duplex structure of martensite,
Crystal grain is fine and closely woven uniformly.
Claims (10)
1. a Nb-Ti system 780MPa level hot-rolled dual-phase steel, it is characterised in that: this steel
Chemical component weight percentage 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.
Nb-Ti system 780MPa level hot-rolled dual-phase steel the most according to claim 1, its
It is characterised by: the chemical component weight percentage of this 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 inevitably impurity.
3. the production of Nb-Ti system 780MPa level hot-rolled dual-phase steel described in a claim 1
Method, including smelting, application of vacuum, continuous casting, the step that heats, roll, cool down and batch,
It is characterized in that: described cooling step uses the cold technique of syllogic control: control first paragraph cooling speed
Degree is 130～180 DEG C/s, is cooled to 610～740 DEG C, and controlling second segment cooling velocity is 3～8
DEG C/s, and it is cooled to 590～720 DEG C, controlling three-stage cooling speed is 50～70 DEG C/s, is cooled to
50～150 DEG C, and control cooler-water temperature be 10～25 DEG C.
The production of Nb-Ti system 780MPa level hot-rolled dual-phase steel the most according to claim 3
Method, it is characterised in that: described milling step uses segmentation rolling, controls roughing end temp
Being 1080～1120 DEG C, controlling finish rolling finishing temperature is 870～910 DEG C.
The production of Nb-Ti system 780MPa level hot-rolled dual-phase steel the most according to claim 3
Method, it is characterised in that: described heating steps, controlling slab heating temperature is 1260～1320
DEG C, the heat time is 60～70min.
6. according to Nb-Ti system 780MPa level hot rolling two-phase described in claim 3 or 4 or 5
The production method of steel, it is characterised in that: described cooling step, controlling first paragraph cooling velocity is
165～180 DEG C/s, being cooled to 610～690 DEG C, controlling second segment cooling velocity is 3～5 DEG C/s,
Being cooled to 590～630 DEG C, controlling three-stage cooling speed is 50～65 DEG C/s, is cooled to 90～100
℃。
7. according to Nb-Ti system 780MPa level hot rolling two-phase described in claim 3 or 4 or 5
The production method of steel, it is characterised in that batch step described in:, controlling coiling temperature is 50～150
℃。
8. according to Nb-Ti system 780MPa level hot rolling two-phase described in claim 3 or 4 or 5
The production method of steel, it is characterised in that: described vacuum processing step, control vacuum processing time
＞ 15min.
9. according to Nb-Ti system 780MPa level hot rolling two-phase described in claim 3 or 4 or 5
The production method of steel, it is characterised in that: described milling step, controlling roughing end temp is
1115～1120 DEG C, controlling finish rolling finishing temperature is 905～910 DEG C.
10. according to Nb-Ti system 780MPa level hot rolling two-phase described in claim 3 or 4 or 5
The production method of steel, it is characterised in that: described heating steps, controlling slab heating temperature is
1290～1320 DEG C, the heat time is 60～70min.
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| CN109694985A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | The 800MPa grade hot rolling biphase plate and its manufacturing method of function admirable |
| WO2020103927A1 (en) * | 2018-11-23 | 2020-05-28 | 宝山钢铁股份有限公司 | High-yield-ratio cold-rolled dual-phase steel and manufacturing method therefor |
| 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 |
| CN115537675A (en) * | 2022-09-15 | 2022-12-30 | 武汉钢铁有限公司 | 800 MPa-grade surface treatment-free steel for commercial vehicles and production method thereof |
| WO2024041539A1 (en) * | 2022-08-23 | 2024-02-29 | 宝山钢铁股份有限公司 | Dual-phase steel and manufacturing method therefor |
| EP4159885A4 (en) * | 2020-05-27 | 2024-04-24 | Baoshan Iron & Steel | 780 mpa-class cold-rolled and annealed dual-phase steel and manufacturing method therefor |
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| 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 |
| WO2024041539A1 (en) * | 2022-08-23 | 2024-02-29 | 宝山钢铁股份有限公司 | Dual-phase steel and manufacturing method therefor |
| CN115537675A (en) * | 2022-09-15 | 2022-12-30 | 武汉钢铁有限公司 | 800 MPa-grade surface treatment-free steel for commercial vehicles and production 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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