CN108396225A - A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method - Google Patents
A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method Download PDFInfo
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- CN108396225A CN108396225A CN201810340842.XA CN201810340842A CN108396225A CN 108396225 A CN108396225 A CN 108396225A CN 201810340842 A CN201810340842 A CN 201810340842A CN 108396225 A CN108396225 A CN 108396225A
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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
- C21D8/0221—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
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
-
- 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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- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention provides a kind of 700MPa grades of titaniferous hot rolling biphase plates and its manufacturing method, chemical component weight percentage content to be：C：0.10 0.15%；Si：0.80 1.20%；Mn：1.20 1.80%；P：≤ 0.020%；S：≤ 0.010%；Ti：0.010 0.040%；Als：≤ 0.060%；Remaining is Fe and is inevitably mingled with.Compared with prior art, use thickness specification produced by the invention for the hot rolled steel plate of 3 4mm, microscopic structure is ferrite+martensite, wherein ferritic volume fraction is 65 75%, Martensite Volume Fraction is 25 35%, and the yield strength of product is 480 550MPa, and tensile strength is 720 820MPa, yield tensile ratio≤0.68, elongation percentage A50It is 20 30%, 180 ° of buckling test D=4a are qualified.
Description
Technical field
The invention belongs to hot-rolled dual-phase steel technical field of producing, and it is double to be related specifically to a kind of 700MPa grades of titaniferous hot rolling
Phase steel plate and its manufacturing method.
Background technology
Critical component one of of the automotive wheel as automobile, will not only bear gravity, brake force, driving force, the vapour of automobile
The lateral force that vehicle generates when turning to, and still suffer from the impact force of Uneven road generation.Therefore, automotive wheel should have light
Matter, high-strength, high rigidity, high fatigue performance etc..
With the rapid development of auto industry, lightweight, energy conservation and environmental protection, safety have become its main trend developed,
This requirement also to wheel performance is higher and higher.Hot-rolled dual-phase steel is due to good strong plasticity, low yield strength ratio, the hardening of high initial manufacture
Rate, good baking and hardening performance and anti-fatigue performance etc., are used for by automobile manufacturing enterprises such as general, Ford, Beijing Jeeps
The manufacture of automotive wheel.Currently, for the hot-rolled dual-phase steel of production and application mainly based on DP540-DP600, DP600 is special both at home and abroad
It is not the dual phase steel of DP780 or more ranks still based on cold rolling.Therefore, the high-strength hot-rolled of 700MPa grades and the above rank is developed
Dual phase steel promotes automotive sheet to have great importance " with hot Dai Leng " application range of expansion hot-rolled dual-phase steel.
About 700MPa grades and patent that the above high-strength dual phase steel of rank hot rolling is declared have it is multinomial.Such as：Publication No.
The patent of CN102912244A discloses a kind of tensile strength 780MPa grades of hot rolling biphase plates and its manufacturing method, chemistry at
Divide and weight percent content 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%, remaining is Fe and can not
Impurity is avoided, it is 840-920 DEG C that continuous coo1ing technique, finishing temperature are used after rolling, and coiling temperature is 500-600 DEG C.Although at
Setting up separately in meter reduces Si contents, can effectively improve surface quality, but add the precious metals such as Cr, Nb, production cost
It is higher, and coiling temperature is higher, cannot avoid the phase change region of bainite completely, be also easy to produce bainite structure, product it is final
Mechanical Fluctuation is larger.
A kind of 700MPa grades of hot-rolled dual-phase steels of patent disclosure and preparation method thereof of 104451402 A of Publication No. CN
A kind of high-strength hot-rolled dual-phase steel of the patent disclosure of (addition 0.60-1.00%Cr), 101603150 A of Publication No. CN
Flexible rolling production method (addition 0.40-0.60%Cr, 0.30-0.40%Mo), 101279330 A of Publication No. CN it is special
A kind of tensile strength 700MPa grades of hot-rolled dual-phase steel board fabrication method (addition 0-0.60%Cr, 0-0.40% disclosed in profit
Mo), 780MPa grades of hot-rolled dual-phase steels of the Cr-Nb systems of the patent disclosure of 105779874 A of Publication No. CN and its production method
A kind of tensile strength >=780MPa grades of the patent disclosure of (addition 0.30-0.49%Cr), 104357744 A of Publication No. CN
Hot-rolled dual-phase steel and production method (addition 0-0.60%Cr) etc., the producer of above 700MPa grades or more of hot-rolled dual-phase steel
Method is added to Cr, Mo precious metal to some extent, causes production cost higher, it is difficult to realize industrialized mass production.
700MPa grades and the above hot-rolled dual-phase steel at present, production method press the height of coiling temperature, can be divided into middle warm rolling
It follows the example of and batches method with low temperature.When medium temperature method for coiling being taken to produce dual phase steel, the conjunctions such as different degrees of addition Cr, Mo are needed in steel
Gold element, production cost is higher cannot to avoid bainitic transformation region completely；And when low temperature being taken to batch method, due to coiling temperature
It is relatively low, higher to the power requirement of coiling machine and roller repairing technique complexity, it is difficult to uniformly be organized and performance.This
A little methods can increase production cost, or be not suitable for, and not have patent to be related to increasing the premise of production cost in unobvious yet at present
Under, by the optimization of rational Design of Chemical Composition and roller repairing coiling technique, good comprehensive performance can be produced
700MPa grades of hot-rolled dual-phase steels.
Invention content
The purpose of the present invention is to provide a kind of 700MPa grades of titaniferous hot rolling biphase plates, do not increase cost, properties of product
It is good.
Another object of the present invention is to provide a kind of manufacturing methods of 700MPa grades of titaniferous hot rolling biphase plate, pass through conjunction
Composition design, smelting, continuous casting, heating, hot rolling, cooling and the design of coiling technique of reason, it is 0.010- that can make amount containing Ti
The hot-rolled dual-phase steel of 0.040%wt% obtains good mechanical property.
Specific technical solution of the present invention is as follows：
A kind of 700MPa grades of titaniferous hot rolling biphase plate, chemical component weight percentage content are：C：0.10-
0.15%；Si：0.80-1.20%；Mn：1.20-1.80%；P：≤ 0.020%；S：≤ 0.010%；Ti：0.010-
0.040%；Als：≤ 0.060%；Remaining is Fe and is inevitably mingled with.
The manufacturing method of above-mentioned 700MPa grades of titaniferous hot rolling biphase plates provided by the invention, including converter smelting, LF stoves
Refining, continuous casting, heating, rolling, cooling and coiling technique.
The heating refers to that strand enters in heating furnace and heated, and heating temperature is 1150-1200 DEG C, and soaking time is
1.5-2h。
The rolling uses two-stage control rolling mill practice, and it is >=60% that reduction ratio is accumulated in roughing, and reduction ratio is accumulated in finish rolling
It is >=70%；Roughing start rolling temperature is 1100-1150 DEG C, and finish rolling finishing temperature is 780-840 DEG C.
Described cooling using three stage control cooling technique, first segment cooling velocity is controlled in 30-50 DEG C/s, final cooling temperature control
System is to 670-700 DEG C, and second segment air cooling time is controlled in 6-10s, and final cooling temperature is controlled to 630-670 DEG C；Three-stage cooling speed
Degree control is cooled to 300-350 DEG C and is batched in 50 DEG C/s or more.
Further, room temperature is air-cooled to after hot-rolled dual-phase steel batches.
Further, the hot-rolled dual-phase steel plate thickness 3-4mm of manufacture.
Further, its microscopic structure of the hot rolling biphase plate of manufacture is ferrite+martensite, wherein ferritic volume
Score is 65-75%, Martensite Volume Fraction 25-35%.
Further, the yield strength of the hot rolling biphase plate of manufacture is 480-550MPa, tensile strength 720-
820MPa, yield tensile ratio≤0.68, elongation percentage A50For 20-30%, 180 ° of buckling test D=4a qualifications.It is bent with lower
It is strong than, higher intensity, preferable extensibility and cold-bending property.
The present invention uses C-Si-Mn component systems in composition design, and adds a small amount of Ti elements, strictly controls P, S etc.
The content of impurity element.C：As the basic element in steel, the intensity to improving steel plays very important by 0.10-0.15%, C
Effect, in order to obtain higher intensity, it is necessary to assure the content of C is 0.10% or more, but C content can not be higher than 0.15%,
Otherwise the ferrite of quantity required for obtaining is difficult in cooling procedure after hot rolling, leads to the moulding poor of steel；Si：0.80-
1.20%, suitable Si is added, the effect of solution strengthening can be not only played, increases the intensity of steel, and ferrite can be promoted
It is formed, expands the process window that ferrite is formed, purify ferrite.When Si this acts on its content and reaches 0.8% or more
It just shows, but the content of Si can not be too high, Si too high levels are easy to generate red scale in steel surface, influence to produce
The surface quality of product；Mn：The intensified element of 1.20-1.80%, Mn as steel can improve the intensity of steel and improve its through hardening
Property, in order to ensure that the intensity of steel, Mn contents should be controlled 1.20% or more, but Mn contents cannot be excessively high, and Mn contents are more than
1.80% can increase the possibility of strand segregation, and be not easy to form required amount of ferrite after rolling, to the forming property of steel
Have an adverse effect.P, S can have an adverse effect to the forming property of steel as impurity element, it should stringent control, content
More lower, better；Als：0.020-0.060%, Als are used mainly as deoxidier, and can play solid solution strengthening effect, if Al
Too high levels can react with the N in steel and coarse AlN particles are precipitated, to the degraded toughness of steel；Ti：0.010-
The effect of 0.040%, Ti in steel mainly plays two, when fining austenite grains, and the ferrite to finally changing
Refining effect is played with martensite；Second is that being combined to form TiN with N element, nitrogen fixation is played.
The present invention is in hot rolling technology design, and for heating and temperature control at 1150-1200 DEG C, main purpose is to take into account surface
Iron scale production quantity and energy consumption, heating temperature is excessively high, due to Si too high levels in steel, reacts at high temperature with FeO, raw
At fayalite (2FeO.SiO2), when temperature be less than 1177 DEG C when, molten iron olivine in solid-state and by FeO firmly anchoring in band
Steel matrix increases the removal difficulty of iron scale, and the red rust that belt steel surface generates is caused to increase, and is unfavorable for improving the surface of strip
Quality；At 780-840 DEG C, lower finishing temperature is conducive to promptly enter ferrite phase region after steel billet rolls finishing temperature control
Part ferrite is precipitated.Three-stage Controlled cooling process is used after rolling：The control of first segment cooling velocity is in 30-50 DEG C/s, eventually
Cold temperature is controlled to 670-700 DEG C, and the purpose is to so that material is quickly entered ferrite transformation region, the prior austenite of refiner material
Body tissue；Second segment air cooling time is controlled in 6-10s, and final cooling temperature is controlled to 630-670 DEG C, certain its purpose is to obtain
The ferritic structure of ratio；The control of third section cooling velocity is in 50 DEG C/s or more, and oiler temperature control is at 300-350 DEG C, mesh
Be the austenite structure fast transition that makes not change be martensitic structure, to make steel finally obtain ferrite+martensite
Duplex structure.
Compared with prior art, the present invention passes through rational composition design, smelting, continuous casting, heating, hot rolling, cooling and volume
The design of taking technique uses thickness specification produced by the invention for the hot rolled steel plate of 3-4mm, and microscopic structure is ferrite+horse
Family name's body, wherein ferritic volume fraction is 65-75%, the yield strength of Martensite Volume Fraction 25-35%, product are
480-550MPa, tensile strength 720-820MPa, yield tensile ratio≤0.68, elongation percentage A50For 20-30%, 180 ° of buckling examinations
D=4a qualifications are tested, there is lower yield tensile ratio, higher intensity, preferable extensibility and cold-bending property.The Thin Specs produced
Hot-rolled dual-phase steel is mainly used for the manufacture of the structural members such as automotive wheel.
Description of the drawings
Fig. 1 is the typical metallographic structure of the present invention.
Specific implementation mode
Embodiment 1
A kind of 700MPa grades of titaniferous hot rolling biphase plate, chemical component weight percentage content are：C：0.15%；Si：
1.11%；Mn：1.74%；P：0.011%；S：0.008%；Ti：0.031%；Als：0.025%；Remaining is Fe and can not keep away
That exempts from is mingled with.As described in Table 1.
The manufacturing method of above-mentioned 700MPa grades of titaniferous hot rolling biphase plate, including converter smelting, the refining of LF stoves, continuous casting, plus
Heat, rolling, cooling and coiling technique.
Heating refers to that strand enters in heating furnace and heated, and heating temperature is 1200 DEG C, soaking time 2h.
Affiliated rolling uses two-stage control rolling mill practice, and it is >=60% that reduction ratio is accumulated in roughing, and reduction ratio is accumulated in finish rolling
It is >=70%；Roughing start rolling temperature is 1146 DEG C, and finish rolling finishing temperature is 823 DEG C.
It is described cooling using three stage control cooling technique, it rolls rear steel plate and is cooled to 692 with the cooling by water speed of 45 DEG C/s
DEG C, it then carries out air-cooled, after air-cooled 6.5s, after being cooled to 665 DEG C, then steel plate is cooled to the cooling by water speed of 54 DEG C/s
347 DEG C are batched.
Room temperature, the hot-rolled dual-phase steel plate thickness 4.0mm of manufacture are air-cooled to after batching.The surrender of the hot rolling biphase plate of manufacture
Intensity is 488MPa, tensile strength 726MPa, yield tensile ratio 0.67, elongation percentage A50It is 26.70%, 180 ° of buckling test D
=4a is qualified.With lower yield tensile ratio, higher intensity, preferable extensibility and cold-bending property.Performance parameter such as the following table 3 institute
Show.
Embodiment 2-3
A kind of 700MPa grades of titaniferous hot rolling biphase plate, chemical component weight percentage content are described in table 1 below.
The manufacturing method of above-mentioned 700MPa grades of titaniferous hot rolling biphase plate, including converter smelting, the refining of LF stoves, continuous casting, plus
Heat, rolling, cooling and coiling technique, specific process parameter are as shown in table 2 below.
The titaniferous hot rolling biphase plate mechanics parameter of manufacture is as shown in table 3 below.
The actual measurement chemical composition (mass percent, wt%) of 1 embodiment of table
The main rolling technological parameter of 2 embodiment of table
The mechanical property of 3 embodiment of table
Titaniferous hot rolling biphase plate produced by the present invention has lower yield tensile ratio, higher intensity, preferable extensibility
And cold-bending property.The Thin Specs hot-rolled dual-phase steel produced is mainly used for the manufacture of the structural members such as automotive wheel.
Claims (8)
1. a kind of 700MPa grades of titaniferous hot rolling biphase plate, which is characterized in that the 700MPa grades of titaniferous hot rolling biphase plate its
Chemical component weight percentage content is：C：0.10-0.15%；Si：0.80-1.20%；Mn：1.20-1.80%；P：≤
0.020%；S：≤ 0.010%；Ti：0.010-0.040%；Als：≤ 0.060%；Remaining is Fe and is inevitably mingled with.
2. a kind of manufacturing method of 700MPa described in claim 1 grades of titaniferous hot rolling biphase plates, including converter smelting, LF stoves
Refining, continuous casting, heating, rolling, cooling and coiling technique, which is characterized in that it is described heating refer to strand enter in heating furnace into
Row heating, heating temperature are 1150-1200 DEG C, soaking time 1.5-2h.
3. manufacturing method according to claim 2, which is characterized in that the rolling uses two-stage control rolling mill practice,
It is >=60% that reduction ratio is accumulated in roughing, and it is >=70% that reduction ratio is accumulated in finish rolling；Roughing start rolling temperature is 1100-1150 DEG C, finish rolling
Finishing temperature is 780-840 DEG C.
4. manufacturing method according to claim 2 or 3, it is characterised in that the cooling uses three stage control cooling technique,
First segment cooling velocity is controlled in 30-50 DEG C/s, and final cooling temperature is controlled to 670-700 DEG C, and second segment air cooling time is controlled in 6-
10s, final cooling temperature are controlled to 630-670 DEG C；The control of third section cooling velocity in 50 DEG C/s or more, be cooled to 300-350 DEG C into
Row batches.
5. manufacturing method according to claim 2 or 3, which is characterized in that hot-rolled dual-phase steel is air-cooled to room temperature after batching.
6. manufacturing method according to claim 2 or 3, which is characterized in that the hot-rolled dual-phase steel plate thickness 3-4mm of manufacture.
7. according to claim 2-6 any one of them manufacturing methods, which is characterized in that its is micro- for the hot rolling biphase plate of manufacture
It is organized as ferrite+martensite, wherein ferritic volume fraction is 65-75%, Martensite Volume Fraction 25-35%.
8. according to claim 2-7 any one of them manufacturing methods, which is characterized in that the surrender of the hot rolling biphase plate of manufacture
Intensity is 480-550MPa, tensile strength 720-820MPa, yield tensile ratio≤0.68, elongation percentage A50For 20-30%, 180 ° of longitudinal directions
Bend test D=4a is qualified.
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| CN109161797A (en) * | 2018-09-06 | 2019-01-08 | 邯郸钢铁集团有限责任公司 | A kind of lightweight endurance hot rolling two-phase wheel steel and its production method |
| CN110257725A (en) * | 2019-07-30 | 2019-09-20 | 马鞍山钢铁股份有限公司 | A kind of high-strength dual phase sheet steel of 980MPa grades of hot rolling and preparation method thereof |
| CN110331326A (en) * | 2019-07-30 | 2019-10-15 | 马鞍山钢铁股份有限公司 | High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof |
| CN110629003A (en) * | 2019-10-22 | 2019-12-31 | 马鞍山钢铁股份有限公司 | Heat treatment-free hot continuous rolling ultrahigh-strength steel plate and manufacturing method thereof |
| CN110760756A (en) * | 2019-11-27 | 2020-02-07 | 河钢股份有限公司邯郸分公司 | Thick DP 680-grade hot-rolled dual-phase steel and preparation method thereof |
| CN113278887A (en) * | 2021-05-14 | 2021-08-20 | 马鞍山钢铁股份有限公司 | 600 MPa-grade high-surface-quality acid-pickling dual-phase steel and manufacturing method thereof |
| CN114990453A (en) * | 2022-05-26 | 2022-09-02 | 天津荣程联合钢铁集团有限公司 | Titanium microalloyed low-alloy high-strength steel and production process thereof |
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| CN110629003A (en) * | 2019-10-22 | 2019-12-31 | 马鞍山钢铁股份有限公司 | Heat treatment-free hot continuous rolling ultrahigh-strength steel plate and manufacturing method thereof |
| CN110760756A (en) * | 2019-11-27 | 2020-02-07 | 河钢股份有限公司邯郸分公司 | Thick DP 680-grade hot-rolled dual-phase steel and preparation method thereof |
| CN113278887A (en) * | 2021-05-14 | 2021-08-20 | 马鞍山钢铁股份有限公司 | 600 MPa-grade high-surface-quality acid-pickling dual-phase steel and manufacturing method thereof |
| CN114990453A (en) * | 2022-05-26 | 2022-09-02 | 天津荣程联合钢铁集团有限公司 | Titanium microalloyed low-alloy high-strength steel and production process thereof |
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