CN107761006B - Strong dual phase steel of low-carbon hot galvanizing superelevation and preparation method thereof - Google Patents
Strong dual phase steel of low-carbon hot galvanizing superelevation and preparation method thereof Download PDFInfo
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- CN107761006B CN107761006B CN201710994645.5A CN201710994645A CN107761006B CN 107761006 B CN107761006 B CN 107761006B CN 201710994645 A CN201710994645 A CN 201710994645A CN 107761006 B CN107761006 B CN 107761006B
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/04—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of bars or wire
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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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- 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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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Abstract
The invention belongs to high-strength steel preparation technical fields, and in particular to a kind of strong dual phase steel of low-carbon hot galvanizing superelevation and preparation method thereof.It is big for the high-strength dual phase steel preparation difficulty of existing cold rolling, equipment requirement is high, problem at high cost, the present invention provides a kind of strong dual phase steel of low-carbon hot galvanizing superelevation and preparation method thereof, dual phase steel composition are as follows: by weight percentage, C:0.05~0.10%, Si:0.20~0.60%, Mn:1.50~2.50%, Cr:0.40~1.00%, Mo:0.10~0.50%, Al:0.02~0.06%, Nb:0.010~0.040%, V:0.10~0.40%, P≤0.015%, S≤0.005%, N≤0.006%, surplus are Fe and inevitable impurity.Smelting molten steel is rolled through smelting-hot rolling-acid when preparation-hot galvanizing-annealing operation after, obtain the strong dual phase steel of low-carbon hot galvanizing superelevation.The strong dual phase steel low cost of low-carbon hot galvanizing superelevation of the invention, mechanical property and zinc-plated function admirable, yield strength are 870~950MPa, and tensile strength is 1200~1280MPa, elongation (A80) it is 6~10%, there is significant economic benefit and social benefit.
Description
Technical field
The invention belongs to automobile high-strength steel preparation technical fields, and in particular to a kind of strong dual phase steel of low-carbon hot galvanizing superelevation
And preparation method thereof.
Background technique
With the development of automotive light weight technology technology, automobile steel develops towards high-strength steel direction has become inexorable trend.It is double
Phase steel is increasingly becoming the first choice of automobile high-strength steel because it has many advantages, such as low yield strength, high-tensile and excellent plasticity
Steel grade, estimated dosage will be more than the 70% of total dosage.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, and receives great attention.
Patent CN 102021482A discloses a kind of cold-rolled galvanized duplex steel and its manufacturing method, preferred chemistry at
Divide percentage are as follows: C:0.095~0.12%, Si:0.60~1.20%, Mn:1.90~2.50%, Cr:0.40~0.60%,
Mo:0.04~0.30%, Nb:0.005~0.025%, Ti:0.01~0.05%, P≤0.010%, S≤0.006%, N≤
0.003%, surplus is Fe and inevitable impurity；Pass through 760~840 DEG C of heat preservations, 1~40 DEG C/s rapid cooling, 450-465 DEG C of rapid cooling
And hot galvanizing is carried out, obtain the hot dip galvanized dual phase steel that tensile strength is greater than 1180MPa.Although by its chemical Composition Control and
Preparation method can obtain the hot dip galvanized dual phase steel of excellent combination mechanical property, but its C, Si content is higher, and welding performance is obvious
It reduces；Hot rolling load is obviously increased after Mo, Ti, Nb are compound simultaneously.
Patent CN 105132817A discloses a kind of 1200MPa grades of cold rolled annealed dual phase steel and its production method, chemistry
Percentage composition are as follows: C:0.14~0.20%, Si:0.2~0.6%, Mn:1.50~2.00%, Cr:0.30~0.70%, Nb:
0.015~0.030%, Ti:0.010~0.030%, P≤0.010%, S≤0.005%, N≤0.005%, surplus be Fe and
Inevitable impurity；Batched by 860~880 DEG C of finish to gauges, 550~680 DEG C, 760~820 DEG C of heat preservations, 630~760 DEG C of slow cooling,
250~300 DEG C of progress Wetted constructures have obtained the cold-rolled biphase steel that tensile strength is greater than 1200MPa.Although passing through its chemistry
Ingredient and preparation method obtain excellent combination mechanical property cold-rolled biphase steel, but its C content is higher, keep its welding performance obvious
It reduces, while Ti, Nb are compound obviously increases hot rolling load.
In conclusion existing invention mainly unilaterally considers the mechanical property of dual phase steel, formability is not comprehensively considered
The factors such as energy, zinc-plated performance and welding performance.
Summary of the invention
The technical problem to be solved in the present invention are as follows: the existing strong dual phase steel of low-carbon hot galvanizing superelevation is difficult to the mechanics having had both
The problem of performance and forming property, zinc-plated performance and welding performance.
The technical solution of present invention solution above-mentioned technical problem are as follows: provide a kind of strong dual phase steel of low-carbon hot galvanizing superelevation and its
Preparation method.The strong dual phase steel of low-carbon hot galvanizing superelevation is mainly made of ferrite, martensite and a small amount of bainite, has low bend
The advantages of taking intensity, high-tensile, excellent plasticity, low production cost, low-carbon-equivalent and good galvanizing surface quality.
The present invention provides a kind of strong dual phase steel of low-carbon hot galvanizing superelevation, chemical components are as follows: by weight percentage, C:
0.05~0.10%, Si:0.20~0.60%, Mn:1.50~2.50%, Cr:0.40~1.00%, Mo:0.10~0.50%,
Al:0.02~0.06%, Nb:0.010~0.040%, V:0.10~0.40%, P≤0.015%, S≤0.005%, N≤
0.006%, surplus is Fe and inevitable impurity.
Preferably, in the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, chemical component are as follows: by weight percentage, C:
0.06~0.09%, Si:0.40~0.60%, Mn:1.80~2.20%, Cr:0.50~0.80%, Mo:0.20~0.40%,
Al:0.02~0.05%, Nb:0.020~0.040%, V:0.20~0.30%, P≤0.012%, S≤0.002%, N≤
0.005%, surplus is Fe and inevitable impurity.
Wherein, in the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, main microstructure is ferrite, martensite and bayesian
Body.
Wherein, in the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, the yield strength of the high-strength dual phase steel is 870~
950MPa, tensile strength are 1200~1280MPa, elongation (A80) it is 6~10%.
The present invention also provides the preparation methods in a kind of above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, including following step
It is rapid:
Smelting molten steel is rolled through smelting-hot rolling-acid-hot galvanizing-annealing operation after, obtain the high-strength dual phase steel of low-carbon cold rolling；
The hot rolling includes heating, dephosphorization, roughing, finish rolling, section cooling and coiling process.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, heating temperature is 1240- in the hot rolling
1280℃。
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, roughing temperature is 1050- in the hot rolling
1100℃。
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, finish rolling start rolling temperature is in the hot rolling
1000~1100 DEG C, finishing temperature is 850~950 DEG C.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, coiling temperature is 600- in the hot rolling
700℃。
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, the acid rolls cold rolling reduction ratio in process
It is 40~60%.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, protection in furnace in the hot galvanizing process
Dew point of atmosphere temperature is -10~-60 DEG C.
Specifically, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, protective atmosphere dew point temperature in the furnace
Degree is made as -10~-25 DEG C being heated to 750 DEG C of temperature or less time controls, is made as -25 being heated to temperature for 750 DEG C or more time controls
~-60 DEG C.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, the annealing operation specifically: from 820
~860 DEG C of speed with 50~80 DEG C/s is quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose, it is zinc-plated after again with 4~10 DEG C/s
Speed be cooled to room temperature eventually.
Compared with prior art, the invention has the benefit that the present invention is in traditional 1200MPa grades of hot dip galvanized dual phase steel base
It on plinth, reduces Mn and increases Cr content to improve its harden ability, and reduce C and mention high Si content to guarantee the sufficiently rich carbon of austenite, together
Shi Caiyong, which pre-oxidizes reducing process, improves surface galvanizing quality.The strong dual phase steel tool of the low-carbon hot galvanizing superelevation that the present invention is prepared
There are low cost, excellent mechanical property and high zinc-plated performance, wherein yield strength is 870~950MPa, tensile strength is 1200~
1280MPa, elongation (A80) it is 6~10%, there is significant economic benefit and social benefit.
Detailed description of the invention
Fig. 1 is the microstructure morphology of hot dip galvanized dual phase steel made from the embodiment of the present invention 1.
Specific embodiment
The present invention provides a kind of strong dual phase steel of low-carbon hot galvanizing superelevation, chemical components are as follows: by weight percentage, C:
0.05~0.10%, Si:0.20~0.60%, Mn:1.50~2.50%, Cr:0.40~1.00%, Mo:0.10~0.50%,
Al:0.02~0.06%, Nb:0.010~0.040%, V:0.10~0.40%, P≤0.015%, S≤0.005%, N≤
0.006%, surplus is Fe and inevitable impurity.
Preferably, in the above-mentioned high-strength dual phase steel of low-carbon hot galvanizing, chemical component are as follows: by weight percentage, C:0.06
~0.09%, Si:0.40~0.60%, Mn:1.80~2.20%, Cr:0.50~0.80%, Mo:0.20~0.40%, Al:
0.02~0.05%, Nb:0.020~0.040%, V:0.20~0.30%, P≤0.012%, S≤0.002%, N≤
0.005%, surplus is Fe and inevitable impurity.
Wherein, in the above-mentioned high-strength dual phase steel of low-carbon hot galvanizing, major alloy is mutually ferrite, martensite and bainite.
Wherein, in the above-mentioned high-strength dual phase steel of low-carbon hot galvanizing, the yield strength of the high-strength dual phase steel is 870~
950MPa, tensile strength are 1200~1280MPa, elongation (A80) it is 6~10%.
In the high-strength dual phase steel of low-carbon cold rolling of the invention, C content is 0.05~0.10%, preferably 0.06~0.09%.
Compared to existing dual phase steel, carbon content is substantially reduced.Known in those skilled in the art, carbon is one of most important component of dual phase steel,
The intensity, plasticity and forming property for determining steel plate, influence greatly solid solution strengthening effect, and C content is dissolved in steel and is increased
0.1%, about 450MPa can be improved in intensity, and when C content is too low, the stability and martensite hardenability of austenite decline, and can lead
Cause low strength.Present invention reduces the carbon contents in dual phase steel, but do not reduce the intensity of dual phase steel, mainly in other yuan
Under the common mating reaction of element, the intensity of dual phase steel is improved.
In addition to C, silicon can be solid-solution in the intensity that steel is improved in ferrite and austenite, and Si can also inhibit carbon in ferrite
The precipitation of compound is enriched with solid solution C atom sufficiently into austenite, to improve its stability.However, when Si too high levels,
The scale on surface that Si is formed in heating furnace is difficult to remove, and increases dephosphorization difficulty.Therefore, intensity and dephosphorization in order to balance
Effect, Si content of the present invention are 0.20~0.60%, preferably 0.40~0.60%.
Manganese is common solution strengthening element in good deoxidier and desulfurizing agent and steel, can be formed in conjunction with C a variety of
Carbide plays the role of precipitation strength, and also dissolving in enhances solid solution strengthening effect in matrix, and Mn easily forms high-melting-point in conjunction with S
Compound MnS improves the hot-working character of steel to eliminate or weaken the hot-short phenomenon due to caused by FeS.Austria can be improved in Mn
Family name's body stability, moves to right C curve, to significantly reduce the critical cooling rate of martensite.Therefore, therefore, manganese of the invention
Content is set as 1.50~2.50%, preferably 1.80~2.20%.
Aluminium can play the role of refining crystal grain, also can inhibit Carbide Precipitation, make the sufficiently rich carbon of austenite.Therefore, this hair
Bright middle Al content is 0.02~0.06%, preferably 0.02~0.05%.
Chromium and molybdenum can significantly postpone pearlite and bainite transformation, and austenite is made sufficiently to be changed into martensitic structure, from
And obtain higher tensile strength.But Mo is much higher compared with the cost of Cr, and the present invention passes through repetition test, show that Cr content is 0.40
~1.00%, have when preferably 0.50~0.80%, Mo content is 0.10~0.50%, preferably 0.20~0.40% higher
Tensile strength, cost performance highest.
Particularly, the present invention also added suitable niobium, and Nb mainly exists in the form of NbC in dual phase steel, have significant
The effect that crystal grain refinement and intergranular precipitation are strengthened.During hot galvanizing annealing heating, undissolved NbC particle being capable of pinning iron element
Body crystal boundary, to play the role of refining crystal grain；When annealing temperature increases to two-phase section, NbC solution temperature is lower, therefore sufficiently molten
Solution is dissolved C atom and is enriched with into austenite to improve its stability in matrix；In cooling procedure, in ferrite
NbC will be precipitated again, to produce apparent precipitation strength.Nb content in the present invention is 0.010~0.050%, preferably
0.020~0.040% is most appropriate.
Vanadium: V mainly exists in the form of VC in dual phase steel, has the function of that significant crystal grain refinement and intergranular precipitation are strengthened.
During hot galvanizing annealing heating, undissolved VC particle can be with pinning ferrite grain boundaries, to play the role of refining crystal grain；
When annealing temperature increases to two-phase section, VC solution temperature is lower, therefore is completely dissolved in matrix, while being dissolved C atom to Ovshinsky
Enrichment is in body to improve its stability；In annealing process, the VC in ferrite will be precipitated again, thus the apparent precipitating of production
Strengthen.In the present invention, V content is 0.10~0.40%, preferably 0.20~0.30%, in dual phase steel of the invention, niobium and vanadium
Action principle it is identical, the two cooperation plays synergistic effect, can more promote the increase of hardness of steel.The addition of one side vanadium can assist
With the effect for promoting niobium, it on the other hand, also can be reduced the usage amount of niobium, reduce production cost.
To sum up, the present invention provides a kind of reasonable strong dual phase steel of low-carbon hot galvanizing superelevation of formula, chemical components are as follows: press
Weight percent meter, C:0.05~0.10%, Si:0.20~0.60%, Mn:1.50~2.50%, Cr:0.40~1.00%,
Mo:0.10~0.50%, Al:0.02~0.06%, Nb:0.010~0.040%, V:0.10~0.40%, P≤0.015%, S
≤ 0.005%, N≤0.006%, surplus are Fe and inevitable impurity.
The present invention also provides a kind of preparation methods of above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, comprising the following steps:
A, it smelts
Smelting molten steel injection electric furnace is smelted, slab is cast as after smelting；
B, hot rolling
Slab obtained by step a by heating, dephosphorization, roughing, finish rolling, section cooling and is batched, hot rolled coil is obtained；It is described
Heating temperature is 1240~1280 DEG C, and roughing temperature is 1050~1100 DEG C, and start rolling temperature is 1000~1100 when the finish rolling
DEG C, finishing temperature is 850~950 DEG C, and coiling temperature is 600~700 DEG C；
C, acid rolls
By hot rolled coil obtained by step b after pickling, it is cold rolled to the Thin Strip Steel of 0.8~2.5mm, wherein cold rolling reduction ratio is 40
~60%；
D, hot galvanizing, annealing
After the resulting strip galvanizing steel of step c, the strong dual phase steel of low-carbon hot galvanizing superelevation is made in annealing.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, the annealing operation specifically: from 820
~860 DEG C of speed with 50~80 DEG C/s is quickly cooled to 440~460 DEG C of temperature of zinc tank furnace nose, it is zinc-plated after again with 4~10 DEG C/s
Speed be cooled to room temperature eventually.
Wherein, in the preparation method of the above-mentioned strong dual phase steel of low-carbon hot galvanizing superelevation, protective atmosphere dew-point temperature is -10 in furnace
~-60 DEG C, dew point, which is -10~-25 DEG C, in 750 DEG C or less heating processes makes surface carry out pre-oxidation to form oxide ferroelectric thin film,
Dew point, which is -25~-60 DEG C, in 750 DEG C or more heating and insulating process makes surface reduction pure iron, to be obviously improved hot galvanizing
The surface galvanizing quality of dual phase steel.
A specific embodiment of the invention will be further explained by embodiment, but not indicated this below
The protection scope of invention is limited in range described in embodiment.
Embodiment 1 prepares the strong dual phase steel of low-carbon hot galvanizing superelevation with the method for the present invention
(1) the hot galvanizing superelevation for constituent as shown in table 1 below being prepared using common smelting process in molten iron is strong
Dual phase steel slab, wherein DP1 is slab 1 prepared by embodiment 1, and DP2 is slab 2 prepared by embodiment 2, and DP3 is the system of embodiment 3
Standby slab 3, DP4 are the slab 4 of comparative example 1 (using the method for CN 102021482A) preparation, and DP5 is that comparative example 2 (uses
The method of CN 105132817A) preparation slab 5.
1 two-phase steel chemical composition (wt.%) of table
| Number | C | Si | Mn | P | S | Als | Cr | Mo | V | Nb | Ti | N |
| DP1 | 0.05 | 0.60 | 2.50 | 0.012 | 0.005 | 0.02 | 0.40 | 0.10 | 0.10 | 0.04 | - | 0.006 |
| DP2 | 0.10 | 0.20 | 1.50 | 0.015 | 0.002 | 0.06 | 1.00 | 0.50 | 0.40 | 0.01 | - | 0.005 |
| DP3 | 0.08 | 0.50 | 2.20 | 0.012 | 0.002 | 0.03 | 0.75 | 0.32 | 0.28 | 0.025 | - | 0.004 |
| CN 102021482A | 0.12 | 0.6 | 2.12 | 0.009 | 0.003 | 0.035 | 0.5 | 0.2 | - | 0.015 | 0.03 | 0.003 |
| CN 105132817A | 0.14 | 0.45 | 2.0 | 0.010 | 0.005 | 0.030 | 0.5 | - | - | 0.03 | 0.015 | 0.005 |
(2) slab is obtained into hot rolled coil after heating, dephosphorization, hot rolling and section cooling, wherein finish rolling start rolling temperature is
1000~1100 DEG C, finishing temperature is 850~950 DEG C, and coiling temperature is 600~700 DEG C；Specific hot-rolled process parameter such as following table
Shown in 2:
2 hot rolling main technologic parameters of table
(3) by after hot rolled coil pickling, be cold rolled to Thin Strip Steel, wherein DP1, DP2, DP3, CN 102021482A and
The cold rolling reduction ratio of CN105132817A is respectively 50.0%, 54.2%, 53.6%, 56.0% and 55.0%.
(4) required product is made in cold-rolled thin steel strip after hot dip galvanizing annealing process is handled, wherein annealing temperature be 820~
860 DEG C, 440~460 DEG C of temperature of zinc tank furnace nose are quickly cooled to from annealing temperature, rapid cooling rate CR1 is 50~80 DEG C/s, plating
It is cooled to room temperature after zinc with the whole cooling rate rate CR2 of 4~10 DEG C/s.Specific hot dip galvanizing annealing process parameter is as shown in table 3:
3 hot galvanizing of table annealing main technologic parameters
| Number | Annealing temperature/DEG C | Rapid cooling rate/DEG C/s | Whole cooling rate rate/DEG C/s |
| DP1 | 860 | 75 | 6.5 |
| DP2 | 820 | 54 | 8.5 |
| DP3 | 850 | 67 | 7.0 |
| CN 102021482A | 770 | 35 | 8.0 |
| CN 105132817A | 820 | - | - |
Its microstructure of the hot dip galvanized dual phase steel prepared through above-mentioned technique is as shown in Figure 1, its mechanical property such as the following table 4 institute
Show:
4 hot dip galvanized dual phase steel mechanical property of table
| Number | Yield strength/MPa | Tensile strength/MPa | Elongation A80/ % | Yield tensile ratio |
| DP1 | 933 | 1224 | 7.8 | 0.76 |
| DP2 | 892 | 1207 | 9.2 | 0.74 |
| DP3 | 908 | 1216 | 8.5 | 0.75 |
| CN 102021482A | 685 | 1208 | 12.0(A50) | 0.57 |
| CN 105132817A | 965 | 1254 | 10.0 | 0.79 |
The result shows that hot dip galvanized dual phase steel microstructure prepared by the present invention is by ferrite, martensite and a small amount of bainite
It forms (see Fig. 1), surface galvanizing quality is good, and tensile strength reaches 1200MPa.Hot dip galvanized dual phase steel C, Mn content of the present invention
It is lower, thus have good welds performance, in combination with pre-oxidation reducing process after have excellent forming property, welding performance
With surface galvanizing quality.
Claims (9)
1. the strong dual phase steel of low-carbon hot galvanizing superelevation, which is characterized in that chemical component are as follows: by weight percentage, C:0.05~
0.10%, Si:0.20~0.60%, Mn:2.20~2.50%, Cr:0.75~1.00%, Mo:0.10~0.50%, Al:
0.02~0.06%, Nb:0.010~0.040%, V:0.28~0.40%, P≤0.015%, S≤0.005%, N≤
0.006%, surplus is Fe and inevitable impurity；Preparation method includes the following steps: smelting molten steel through smelting-hot rolling-acid
Roll-hot galvanizing-annealing operation after, obtain the high-strength dual phase steel of low-carbon cold rolling；The hot rolling include heating, dephosphorization, roughing, finish rolling,
Section cooling and coiling process；The annealing operation specifically: be quickly cooled down from 820~860 DEG C of speed with 54~80 DEG C/s
To 440~460 DEG C of temperature of zinc tank furnace nose, room temperature is cooled to eventually with the speed of 4~10 DEG C/s again after zinc-plated.
2. the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 1, which is characterized in that chemical component are as follows: by weight
Percentages, C:0.06~0.09%, Si:0.40~0.60%, Mn:2.20~2.50%, Cr:0.75~1.00%, Mo:
0.20~0.40%, Al:0.02~0.05%, Nb:0.020~0.040%, V:0.28~0.40%, P≤0.012%, S≤
0.002%, N≤0.005%, surplus are Fe and inevitable impurity.
3. the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 1 or 2, it is characterised in that: microstructure is iron element
Body, martensite and bainite.
4. the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 3, it is characterised in that: the high-strength dual phase steel is bent
Taking intensity is 870~950MPa, and tensile strength is 1200~1280MPa, elongation A80It is 6~10%.
5. the preparation method in the described in any item strong dual phase steels of low-carbon hot galvanizing superelevation of claim 1-4, which is characterized in that packet
Include following steps:
Smelting molten steel is rolled through smelting-hot rolling-acid-hot galvanizing-annealing operation after, obtain the high-strength dual phase steel of low-carbon cold rolling；It is described
Hot rolling includes heating, dephosphorization, roughing, finish rolling, section cooling and coiling process.
6. the preparation method in the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 5, it is characterised in that: the heat
Rolling middle heating temperature is 1240-1280 DEG C；Roughing temperature is 1050-1100 DEG C in the hot rolling；Finish rolling open rolling in the hot rolling
Temperature is 1000~1100 DEG C, and finishing temperature is 850~950 DEG C；Coiling temperature is 600-700 DEG C in the hot rolling.
7. the preparation method in the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 5, it is characterised in that: the acid
Rolling cold rolling reduction ratio in process is 40~60%.
8. the preparation method in the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 5, it is characterised in that: above-mentioned low
In the preparation method of the strong dual phase steel of carbon hot galvanizing superelevation, in the hot galvanizing process in furnace protective atmosphere dew-point temperature be -10~-
60℃。
9. the preparation method in the strong dual phase steel of low-carbon hot galvanizing superelevation according to claim 5, it is characterised in that: described to move back
Firer's sequence specifically: 440~460 DEG C of temperature of zinc tank furnace nose are quickly cooled to from 820~860 DEG C of speed with 50~80 DEG C/s,
Room temperature is cooled to eventually with the speed of 4~10 DEG C/s again after zinc-plated.
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| CN108913998B (en) * | 2018-07-19 | 2021-04-16 | 首钢集团有限公司 | Cold-rolled dual-phase steel and preparation method thereof |
| CN109868416A (en) * | 2019-03-29 | 2019-06-11 | 本钢板材股份有限公司 | A kind of production technology of low cost hot dip galvanized dual phase steel DP590 |
| CN110331341B (en) * | 2019-08-21 | 2021-05-11 | 攀钢集团攀枝花钢铁研究院有限公司 | High-formability high-strength hot-galvanized dual-phase steel and production method thereof |
| CN110358967A (en) * | 2019-08-21 | 2019-10-22 | 攀钢集团攀枝花钢铁研究院有限公司 | Think gauge hot galvanizing Multiphase Steel and its production method |
| CN111438189B (en) * | 2020-04-09 | 2021-12-07 | 北京首钢股份有限公司 | Cold-rolled sheet and shape control method thereof |
| CN113737108A (en) * | 2020-05-27 | 2021-12-03 | 宝山钢铁股份有限公司 | Delay cracking resistant electro-galvanized super-strong dual-phase steel and manufacturing method thereof |
| CN113604728A (en) * | 2021-06-24 | 2021-11-05 | 武汉钢铁有限公司 | High-surface-quality hot-galvanized high-strength steel and manufacturing method thereof |
| CN114574674A (en) * | 2022-02-24 | 2022-06-03 | 山东钢铁集团日照有限公司 | Preparation method capable of simultaneously producing continuous annealing and galvanized DP780 dual-phase steel |
| CN116288042B (en) * | 2023-02-21 | 2024-06-11 | 包头钢铁（集团）有限责任公司 | Hot-rolled steel with tensile strength greater than 700MPa and thickness of 2-4mm for automobile structure and production method thereof |
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| CN105603325B (en) * | 2016-03-23 | 2017-09-29 | 攀钢集团攀枝花钢铁研究院有限公司 | A kind of 600MPa grades of hot dip galvanized dual phase steel containing vanadium and preparation method thereof |
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