CN107747039A - A kind of high reaming performance cold-rolled biphase steel and preparation method thereof - Google Patents
A kind of high reaming performance cold-rolled biphase steel and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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 high reaming performance cold-rolled biphase steel and preparation method thereof, belong to field of steel metallurgy.A kind of high reaming performance cold-rolled biphase steel, by weight percentage, its chemical composition is：C：0.03~0.08%, Si：0.10~0.50%, Mn：1.60~2.00%, V：0.01~0.03%, Al：0.02~0.06%, P≤0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.The preparation method of above-mentioned high reaming performance cold-rolled biphase steel, comprises the following steps：A, smelting procedure；B, hot-rolled process；C, acid rolls process；D, continuous annealing process.Trace V separates out the effect for playing precipitation strength in the form of VC in the present invention；C content is reduced to obtain excellent comprehensive mechanical property simultaneously, cold-rolled biphase steel forming property, welding performance and reaming function admirable, there is significant economic benefit and social benefit.
Description
Technical field
The invention belongs to field of steel metallurgy, and in particular to a kind of high reaming performance cold-rolled biphase steel and preparation method thereof.
Background technology
With the development of automotive light weight technology technology, automobile steel develops towards high-strength steel direction turns into inexorable trend.It is double
Phase steel has the characteristics that low yield strength, high-tensile and excellent plasticity, turns into automobile using first choice high-strength steel, and its dosage is pre-
Meter will be more than 70% in the advanced high-strength steel of automobile using.With the continuous release of internal vapor sweep production capacity, high-strength steel market it is competing
Strive also more and more fierce, the dual phase steel of low-cost and high-performance has become the target that each enterprise is pursued, of great interest.
Patent (CN 102747275A) discloses Large strain and strengthens performance cold-rolled biphase steel and its production method, its chemistry
Percentage composition is：C：0.10~0.15%, Mn：1.0~2.0%, Al：1.0~2.0%, Mo：0.1~0.2%, surplus is
Fe and inevitable impurity；By 800~840 DEG C of finish to gauges, 600-650 DEG C batch, 810~850 DEG C insulation, 260~280 DEG C
Wetted constructures, the cold-rolled biphase steel that tensile strength is more than 600MPa is obtained.Although pass through its chemical composition and production method
The cold-rolled biphase steel of preparation has excellent mechanical property, but yield strength is higher, influences the forming property of material.Due to needing
A large amount of Al, Mo are added, not only production cost are substantially increased, continuous casting and rolling difficulty improve.In addition, C content increase makes
Obtain cold-rolled biphase steel welding performance to decline, finally necessarily affect extensive use of the dual phase steel on automobile.
Patent (CN 104109814A), which discloses one kind, has flanging property hot dip galvanized dual phase steel plate and manufacture method, its
Chemical composition percentage is：C：0.065~0.085%, Si：0.40~0.55%, Mn：1.55~1.65%, P≤
0.018%, S≤0.010%, Al：0.03~0.05%, Cr：0.35~0.55%, Nb：0.03~0.04%, N≤
0.005%, surplus is Fe and inevitable impurity；By 890~950 DEG C of finish to gauges, 560~650 DEG C batch, 780~840 DEG C
Insulation, the hot dip galvanized dual phase steel that tensile strength is more than 600MPa, the hot dip galvanized dual phase steel reaming produced by this method are obtained
Rate is 45~50%.However, the dual phase steel needs 0.03~0.04%Nb of addition, production cost is set substantially to increase, while reaming
Rate is still treated further to improve.
Patent (CN 103952523A) discloses a kind of continuous annealing side of martensite ferrite dual phase steel cold rolled sheet
Method, its chemical composition percentage are：C：0.06~0.09%, Si：0.18~0.49%, Mn：1.65~1.90%, Cr：0.15
~0.18%, Als：0.03~0.05%, P≤0.02%, S≤0.004%, surplus are Fe and inevitable impurity；Pass through
760~840 DEG C of insulations, 660~700 DEG C of slow cooling, 60~100 DEG C/s be cooled to soon 250~270 DEG C, 30~100 DEG C/s bis- times plus
It is 695-710MPa cold-rolled biphase steels that heat obtains tensile strength to the method for 310~380 DEG C of Wetted constructures.This method is given birth to
The cold-rolled biphase steel of production has excellent comprehensive mechanical property and forming property, but continuous annealing process is complicated, it is necessary to quick
Cooling and quick heating, it is higher to equipment Requirement；Microalloy element addition simultaneously is more so that production cost increase.
The content of the invention
It is an object of the invention to reduce the production cost of cold-rolled biphase steel, while improve its forming properties, welding performance
And production difficulty.
Technical scheme is to provide a kind of high reaming performance cold-rolled biphase steel used by the present invention realizes above-mentioned purpose, by weight
Percentages are measured, its chemical composition is：C：0.03~0.08%, Si：0.10~0.50%, Mn：1.60~2.00%, V：
0.01~0.03%, Al：0.02~0.06%, P≤0.020%, S≤0.015%, N≤0.006%, surplus are Fe and can not
Avoid impurity.
Preferably, in high reaming performance cold-rolled biphase steel described above, by weight percentage, its chemical composition is：
C：0.04~0.06%, Si：0.20~0.40%, Mn：1.80~2.00%, V：0.01~0.03%, Al：0.03~
0.05%, P≤0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.
Wherein, in high reaming performance cold-rolled biphase steel described above, the surrender of the high reaming performance cold-rolled biphase steel
Intensity is 340~380MPa, and tensile strength is 590~630MPa, elongation A80For 25.0~30.0%, hole expansibility 55-
70%.
Present invention also offers the preparation method of above-mentioned high reaming performance cold-rolled biphase steel, comprise the following steps：
A, smelting procedure：Smelted according to the chemical composition of high reaming performance cold-rolled biphase steel, by being cast as slab；
B, hot-rolled process：Slab is obtained into hot rolled coil after heating, dephosphorization, roughing, finish rolling and section cooling；
C, acid rolls process：By hot rolled coil after overpickling, cold rolling turns into cold-rolled thin steel strip；
D, continuous annealing process：By cold-rolled thin steel strip after continuous annealing, high reaming performance cold-rolled biphase steel is made.
Wherein, in the preparation method of high reaming performance cold-rolled biphase steel described above, in step B, the hot-rolled process
Middle heating-up temperature is 1200~1260 DEG C, and finish rolling start rolling temperature is 1000~1100 DEG C, and finishing temperature is 850~950 DEG C, volume
It is 600~700 DEG C to take temperature, and hot rolled thickness is 2.5~4.0mm.
Wherein, in the preparation method of high reaming performance cold-rolled biphase steel described above, in step C, the acid rolls process
Middle cold rolling reduction ratio is 50~70%.
Wherein, in the preparation method of high reaming performance cold-rolled biphase steel described above, in step D, the continuous annealing
Concrete operations be：Cold-rolled thin steel strip is first cooled to 630 from 780~820 DEG C of annealing temperature with 1~5 DEG C/s slow cooling speed
~680 DEG C, 250~350 DEG C are cooled to 10~50 DEG C/s rapid cooling speed immediately, is finally cooled to room temperature.
The beneficial effects of the invention are as follows：
The invention provides a kind of high reaming performance cold-rolled biphase steel, micro- by controlling component content in steel
Amount V separates out the effect for playing precipitation strength in the form of VC, steel is had excellent performance, its yield strength for 340~
380MPa, yield tensile ratio are≤0.60, and tensile strength is 590~630MPa, elongation (A80) it is 25.0~30.0%, hole expansibility
For 55-70%：Yield strength and yield tensile ratio are relatively low, therefore forming property is excellent；C content reduces, therefore welding performance is excellent；Low C contains
Amount high Mn content reduces ferrite/martensite intensity difference, therefore reaming flange excellent performance；In addition, V comes in the present invention
Source is that original molten iron V content is controlled in converter, rather than additionally adds vanadium iron, hence it is evident that reduces production cost；In addition,
Steel of the present invention is not added with Mo, Cr of costliness, reduce further production cost.
Brief description of the drawings
Fig. 1 is the microstructure morphology of cold-rolled biphase steel of the present invention.
Embodiment
Specifically, a kind of high reaming performance cold-rolled biphase steel, by weight percentage, its chemical composition is：C：0.03~
0.08%, Si：0.10~0.50%, Mn：1.60~2.00%, V：0.01~0.03%, Al：0.02~0.06%, P≤
0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.
The present invention is high, and reaming performance cold-rolled biphase steel design of alloy principle is as follows：
C content is 0.03~0.08% in steel of the present invention：C determines steel plate as one of most important component of dual phase steel
Intensity, plasticity and forming property；C is the most obvious element of solid solution strengthening effect in ferrous materials, and practice is found, C content mistake
When low, the stability and martensite hardenability of austenite decline, and cause low strength, are typically not less than 0.02% in dual phase steel,
In addition, being dissolved C content increase by 0.1% in steel, its intensity can improve about 450MPa；When single C content is too high, the plasticity of dual phase steel
Decline with welding performance, 0.20% is generally not more than in dual phase steel；Consider influences of the C to Steel Properties, it is preferred that C content
For 0.04~0.06%.
Si can be solid-solution in the intensity that steel is improved in ferrite and austenite, and its effect is only second to C, P, compared with Mn, Cr, Ti and
The elements such as Ni are strong；Si can also suppress the precipitation of carbide in ferrite, solid solution C atoms is fully enriched with into austenite, from
And improve its stability.However, during Si too high levels, the scale on surface that Si is formed in heating furnace is very difficult to remove, increase
Dephosphorization difficulty；The present invention, to avoid increasing de-scaling difficulty, increases production cost, designs Si contents when considering steel stability
For 0.10~0.50%, preferably 0.20~0.40%.
Mn is the solution strengthening element commonly used in good deoxidier and desulfurizing agent, and steel, general not low in dual phase steel
In 1.20%；Mn can both combine to form a variety of carbide with C and play a part of precipitation strength, and also dissolving in matrix strengthens admittedly
Molten reinforcing effect；Mn easily combines to form high melting compound MnS with S, hot-short existing caused by FeS so as to eliminate or weaken
As improving the hot-working character of steel；Mn can improve stabilization of austenite, move to right C curve, so as to significantly reduce martensite
Critical cooling rate；Therefore, Mn contents are 1.60~2.00%, preferably 1.80~2.00% in the present invention.
V content is that 0.01~0.03%, V mainly exists in dual phase steel in the form of VC in steel of the present invention, is had significantly brilliant
The effect that grain refinement and intergranular precipitation are strengthened；In continuous annealing heating process, undissolved VC particles can be brilliant with pinning ferrite
Boundary, so as to play a part of crystal grain thinning；When annealing temperature increases to two-phase section, VC solution temperatures are relatively low, therefore are completely dissolved in
In matrix, while it is dissolved C atoms and is enriched with into austenite to improve its stability；In annealing process, the VC in ferrite will
Again separate out, so as to produce obvious precipitation strength.
Al is deoxidier common in steel, while can form AlN pinning crystal boundaries, so as to play a part of crystal grain thinning；
In addition, Al is similar to Si effects, Carbide Precipitation can be suppressed, so that the fully rich carbon of austenite；Al content in steel of the present invention
For 0.02~0.06%, preferably 0.03~0.05%.
The present invention reduces C content and carries high Mn content to ensure its through hardening on the basis of traditional 590MPa levels cold-rolled biphase steel
Property, so as to obtain excellent reaming flange performance, forming property and welding performance.Therefore, high reaming performance cold rolling of the invention
Dual phase steel has an excellent comprehensive mechanical property, and wherein yield strength is 340~380MPa, and tensile strength is 590~
630MPa, elongation (A80) it is 25.0~30.0%, hole expansibility 55-70%.
Present invention also offers the preparation method of above-mentioned high reaming performance cold-rolled biphase steel, comprise the following steps：
A, smelting procedure：Smelted according to the chemical composition of high reaming performance cold-rolled biphase steel, by being cast as slab；
B, hot-rolled process：Slab is obtained into hot rolled coil after heating, dephosphorization, roughing, finish rolling and section cooling；
C, acid rolls process：By hot rolled coil after overpickling, cold rolling turns into cold-rolled thin steel strip；
D, continuous annealing process：By cold-rolled thin steel strip after continuous annealing, high reaming performance cold-rolled biphase steel is made.
In the preparation method of high reaming performance cold-rolled biphase steel described above, in smelting procedure, controlled in converter former
There is molten iron V content, rather than additionally add vanadium iron
In the preparation method of high reaming performance cold-rolled biphase steel described above, heating-up temperature is in the hot-rolled process
1200~1260 DEG C, finish rolling start rolling temperature be 1000~1100 DEG C, finishing temperature be 850~950 DEG C, coiling temperature be 600~
700 DEG C, hot rolled thickness is 2.5~4.0mm.
In the preparation method of high reaming performance cold-rolled biphase steel described above, the acid rolls cold rolling reduction ratio in process and is
50~70%.
In the preparation method of high reaming performance cold-rolled biphase steel described above, the concrete operations of the continuous annealing are：
Cold-rolled thin steel strip is first cooled to 630~680 DEG C from 780~820 DEG C of annealing temperature with 1~5 DEG C/s slow cooling speed, immediately with
10~50 DEG C/s rapid cooling speed is cooled to 250~350 DEG C, is finally cooled to room temperature.
Preferably, a kind of high reaming performance cold-rolled biphase steel, by weight percentage, its chemical composition is：C：0.04~
0.06%, Si：0.20~0.40%, Mn：1.80~2.00%, V：0.01~0.03%, Al：0.03~0.05%, P≤
0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.
Preferably, the preparation method of above-mentioned high reaming performance cold-rolled biphase steel, comprises the following steps：
A, smelting procedure：Smelted according to the chemical composition of high reaming performance cold-rolled biphase steel, by being cast as slab；
B, hot-rolled process：Slab is obtained into hot rolled coil after heating, dephosphorization, roughing, finish rolling and section cooling；Wherein,
Heating-up temperature is 1200~1260 DEG C, and finish rolling start rolling temperature is 1000~1100 DEG C, and finishing temperature is 850~950 DEG C, batches temperature
Spend for 600~700 DEG C, hot rolled thickness is 2.5~4.0mm；
C, acid rolls process：By hot rolled coil after overpickling, cold rolling turns into cold-rolled thin steel strip；Wherein, acid rolls cold rolling in process
Reduction ratio is 50~70%；
D, continuous annealing process：By cold-rolled thin steel strip from 780~820 DEG C of annealing temperature, elder generation is with 1~5 DEG C/s slow cooling speed
Rate is cooled to 630~680 DEG C, is cooled to 250~350 DEG C with 10~50 DEG C/s rapid cooling speed immediately, is finally cooled to room
Temperature, high reaming performance cold-rolled biphase steel is made.
The present invention is described in further detail below by embodiment, but therefore not limited the scope of the present invention
Among described scope of embodiments.
Embodiment 1
Two groups high reaming performance cold-rolled biphase steel is present embodiments provided, it is as shown in table 1 that it is melted into composition；
The cold-rolled biphase steel chemical composition (wt.%) of 1 embodiment of table 1
| Numbering | C | Si | Mn | P | S | Als | V | N |
| 1 | 0.04 | 0.40 | 1.90 | 0.011 | 0.006 | 0.040 | 0.03 | 0.004 |
| 2 | 0.05 | 0.30 | 1.95 | 0.012 | 0.004 | 0.035 | 0.02 | 0.005 |
The preparation method of above-mentioned high reaming performance cold-rolled biphase steel, concrete technology are as follows：
A, smelting procedure：By smelting process, the dual phase steel slab of chemical composition as shown in table 1 below is prepared, wherein turning
Original molten iron V content is controlled in stove, rather than additionally adds vanadium iron；
B, hot-rolled process：Slab is obtained into hot rolled coil, specific Hot-roller after heating, dephosphorization, hot rolling and section cooling
Skill parameter is as shown in table 2 below；
The cold-rolled biphase steel hot rolling main technologic parameters of 2 embodiment of table 1
C, acid rolls process：After hot rolled coil pickling, Thin Strip Steel is cold rolled to, wherein the Thin Strip Steel thickness of numbering 1 is 1.4mm,
Cold rolling reduction ratio is 65.0%；The Thin Strip Steel thickness 1.2mm of numbering 2, cold rolling reduction ratio are 65.7%；
D, continuous annealing process：Required product is made after continuous annealing process is handled in cold-rolled thin steel strip, wherein annealing
Temperature is 780~820 DEG C, and 630~680 DEG C of rapid cooling start temperature is slowly cooled to from annealing temperature, and its slow cooling speed is 1~5
DEG C/s, 250~350 DEG C of overaging temperature is quickly cooled to immediately, and its rapid cooling speed is 10~50 DEG C/s, is finally cooled to room
Temperature；Specific continuous annealing process parameter is as shown in table 3：
The continuous annealing main technologic parameters of 3 embodiment of table 1
Cold-rolled biphase steel its microstructure prepared through above-mentioned technique is as shown in figure 1, according to GB/T228-2010《Metal material
Expect tensile testing at ambient temperature》Above-mentioned cold-rolled biphase steel performance is tested, its mechanical property is as shown in table 4 below：
The cold-rolled biphase steel mechanical property of 4 embodiment of table 1
Note：Ceq=C+Si/20+Mn/30+2P+4S, Ceq are carbon equivalent, represent the welding performance of steel；Ceq is lower, welding
Performance is better.
As a result showing, cold rolling high-strength steel microstructure prepared by the embodiment of the present invention is made up of ferrite and martensite, its
Middle yield strength (340~380MPa) and yield tensile ratio (≤0.60) are relatively low, tensile strength (590-630MPa), elongation (25.0
~30.0%) and hole expansibility (55~70%) is higher, while cold-rolled biphase steel C content is relatively low, so with excellent hole expandability
Energy, forming property and welding performance, can be widely applied to automobile structure and reinforcer.
Claims (7)
1. high reaming performance cold-rolled biphase steel, it is characterised in that：By weight percentage, its chemical composition is：C：0.03~
0.08%, Si：0.10~0.50%, Mn：1.60~2.00%, V：0.01~0.03%, Al：0.02~0.06%, P≤
0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.
2. high reaming performance cold-rolled biphase steel according to claim 1, it is characterised in that：By weight percentage, it is changed
Study and be divided into：C：0.04~0.06%, Si：0.20~0.40%, Mn：1.80~2.00%, V：0.01~0.03%, Al：
0.03~0.05%, P≤0.020%, S≤0.015%, N≤0.006%, surplus are Fe and inevitable impurity.
3. high reaming performance cold-rolled biphase steel according to claim 1 or 2, it is characterised in that：The high reaming performance is cold
The yield strength for rolling dual phase steel is 340~380MPa, and tensile strength is 590~630MPa, elongation A80For 25.0~30.0%,
Hole expansibility is 55-70%.
4. the preparation method of the high reaming performance cold-rolled biphase steel described in any one of claims 1 to 3, it is characterised in that：Including
Following steps：
A, smelting procedure：Smelted according to the chemical composition of high reaming performance cold-rolled biphase steel, by being cast as slab；
B, hot-rolled process：Slab is obtained into hot rolled coil after heating, dephosphorization, roughing, finish rolling and section cooling；
C, acid rolls process：By hot rolled coil after overpickling, cold rolling turns into cold-rolled thin steel strip；
D, continuous annealing process：By cold-rolled thin steel strip after continuous annealing, high reaming performance cold-rolled biphase steel is made.
5. the preparation method of high reaming performance cold-rolled biphase steel according to claim 4, it is characterised in that：In step B, institute
It is 1200~1260 DEG C to state in hot-rolled process heating-up temperature, and finish rolling start rolling temperature is 1000~1100 DEG C, finishing temperature is 850~
950 DEG C, coiling temperature is 600~700 DEG C, and hot rolled thickness is 2.5~4.0mm.
6. the preparation method of high reaming performance cold-rolled biphase steel according to claim 4, it is characterised in that：In step C, institute
It is 50~70% to state acid to roll cold rolling reduction ratio in process.
7. the preparation method of high reaming performance cold-rolled biphase steel according to claim 4, it is characterised in that：In step D, institute
The concrete operations for stating continuous annealing are：Cold-rolled thin steel strip is from 780~820 DEG C of annealing temperature, and elder generation is with 1~5 DEG C/s slow cooling speed
630~680 DEG C are cooled to, 250~350 DEG C is cooled to 10~50 DEG C/s rapid cooling speed immediately, is finally cooled to room temperature.
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108754307A (en) * | 2018-05-24 | 2018-11-06 | 山东钢铁集团日照有限公司 | A method of producing the economical cold rolling DP780 steel of different yield strength ranks |
| CN109943778A (en) * | 2019-04-30 | 2019-06-28 | 马鞍山钢铁股份有限公司 | A kind of 590MPa that reaming is had excellent performance grade cold-rolled biphase steel and its production method |
| CN110643894A (en) * | 2018-06-27 | 2020-01-03 | 宝山钢铁股份有限公司 | Ultra-high strength hot rolled steel sheet and steel strip having good fatigue and hole expansion properties, and method for manufacturing same |
| CN111187893A (en) * | 2020-02-24 | 2020-05-22 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for enhancing uniformity of 780DP high-hole-expansion cold-rolled dual-phase steel |
| CN111206186A (en) * | 2020-02-24 | 2020-05-29 | 攀钢集团攀枝花钢铁研究院有限公司 | High-hole-expansion-performance cold-rolled dual-phase steel with tensile strength of 780MPa and preparation method thereof |
| CN111206187A (en) * | 2020-02-24 | 2020-05-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Flexible production method of 780 MPa-tensile-strength high-reaming cold-rolled dual-phase steel |
| CN111438189A (en) * | 2020-04-09 | 2020-07-24 | 北京首钢股份有限公司 | Cold-rolled sheet and shape control method thereof |
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Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108754307A (en) * | 2018-05-24 | 2018-11-06 | 山东钢铁集团日照有限公司 | A method of producing the economical cold rolling DP780 steel of different yield strength ranks |
| CN108754307B (en) * | 2018-05-24 | 2020-06-09 | 山东钢铁集团日照有限公司 | Method for producing economical cold-rolled DP780 steel with different yield strength grades |
| CN110643894A (en) * | 2018-06-27 | 2020-01-03 | 宝山钢铁股份有限公司 | Ultra-high strength hot rolled steel sheet and steel strip having good fatigue and hole expansion properties, and method for manufacturing same |
| CN110643894B (en) * | 2018-06-27 | 2021-05-14 | 宝山钢铁股份有限公司 | Ultra-high strength hot rolled steel sheet and steel strip having good fatigue and hole expansion properties, and method for manufacturing same |
| CN109943778A (en) * | 2019-04-30 | 2019-06-28 | 马鞍山钢铁股份有限公司 | A kind of 590MPa that reaming is had excellent performance grade cold-rolled biphase steel and its production method |
| CN109943778B (en) * | 2019-04-30 | 2020-08-11 | 马鞍山钢铁股份有限公司 | 590 MPa-grade cold-rolled dual-phase steel with excellent hole expansion performance and production method thereof |
| CN111187893A (en) * | 2020-02-24 | 2020-05-22 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for enhancing uniformity of 780DP high-hole-expansion cold-rolled dual-phase steel |
| CN111206186A (en) * | 2020-02-24 | 2020-05-29 | 攀钢集团攀枝花钢铁研究院有限公司 | High-hole-expansion-performance cold-rolled dual-phase steel with tensile strength of 780MPa and preparation method thereof |
| CN111206187A (en) * | 2020-02-24 | 2020-05-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Flexible production method of 780 MPa-tensile-strength high-reaming cold-rolled dual-phase steel |
| CN111187893B (en) * | 2020-02-24 | 2021-06-29 | 攀钢集团攀枝花钢铁研究院有限公司 | Method for enhancing uniformity of 780DP high-hole-expansion cold-rolled dual-phase steel |
| CN111438189A (en) * | 2020-04-09 | 2020-07-24 | 北京首钢股份有限公司 | Cold-rolled sheet and shape control method thereof |
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