CN106574341A

CN106574341A - High-strength steel sheet and production method for same, and production method for high-strength galvanized steel sheet

Info

Publication number: CN106574341A
Application number: CN201580042276.9A
Authority: CN
Inventors: 川崎由康; 松田广志; 小幡美绘; 金子真次郎; 横田毅; 濑户洋; 濑户一洋
Original assignee: NKK Corp
Current assignee: JFE Steel Corp; JFE Engineering Corp
Priority date: 2014-08-07
Filing date: 2015-08-05
Publication date: 2017-04-19
Anticipated expiration: 2035-08-05
Also published as: WO2016021193A1; US20170204490A1; JP5983896B2; EP3178953A1; MX2017001720A; EP3178953A4; JPWO2016021193A1; CN106574341B

Abstract

The present invention provides a high-strength steel sheet having a tensile strength (TS) of at least 780 MPa, excellent ductility and stretch flangeability, and excellent material-quality stability, achieved by: having a specific component composition; the steel structure having, in terms of area ratio, a total of ferrite and bainitic ferrite of 25-80%, and 3-20% martensite, and having, in terms of volume fraction, at least 10% retained austenite; the average crystalline particle diameter of the retained austenite being not more than 2[mu]m; the average Mn volume (mass%) in the retained austenite being at least 1.2 times the Mn volume (mass%) in the steel; and the area ratio of retained austenite that has an average C volume (mass%) of at least 2.1 times the C volume (mass%) of the steel being at least 60% of the area ratio of the total retained austenite.

Description

The manufacture method of high-strength steel sheet and its manufacture method and high strength galvanized steel plate

Technical field

The present invention relates to be primarily suitable for the high-strength steel sheet having excellent moldability and its manufacturer of the structural elements of automobile Method, will particularly obtain the tensile strength (TS) with more than 780MPa, not only ductility is excellent but also stretch flangeability is also excellent The excellent high-strength steel sheet of good and stable material quality.

Background technology

In recent years, in order to ensure crew member during collision security, improve the fuel effect that body lightening brought Rate, it is more than 780MPa just energetically to advance tensile strength (TS) and the relatively thin high-strength steel sheet of its thickness of slab is applied to automobile The dynamic of structural elements.

And, recently, also research has answering for the high high-strength steel sheet of 980MPa levels, the intensity of the TS of 1180MPa levels With.

But, it is however generally that, the high intensity of steel plate can cause the reduction of formability, accordingly, it is difficult to take into account high intensity and Excellent formability, expects there is the steel plate of high intensity and excellent formability simultaneously.

In addition, the shape freezing of steel plate is significantly reduced due to high intensity, the thin-walled property of steel plate, it is this in order to tackle Situation, extensively carries out following method：Change in shape when stamping after the prediction demoulding in advance, designs its change in shape amount Estimate in interior mould.

But, the change in shape amount is predicted based on TS, therefore, when the TS of steel plate fluctuates, the shape predicted becomes Change value increases with the deviation of the change in shape amount of reality, so as to induce shape defect.And, the steel plate for forming the shape defect exists The amendment that sheet metal processing etc. is carried out to shape one by one is needed after stamping, volume production efficiency is significantly reduced.Therefore, Ask the fluctuation of the TS for reducing steel plate as much as possible.

Then, for the requirement, for example, Patent Document 1 discloses a kind of processability and shape freezing is excellent High-strength steel sheet, it is characterised in that contain C in terms of quality %：More than 0.06% and less than 0.60%, Si+Al：More than 0.5% And less than 3.0%, Mn：More than 0.5% and less than 3.0%, P：Less than 0.15%, S：Less than 0.02%, also, with tempering horse Family name's body phase for the area occupation ratios of whole tissues be more than 15%, ferritic phase for the area occupation ratios of whole tissues be more than 5% and Less than 60%, retained austenite is more than 5% relative to the volume fraction of all tissues and can contain bainite and/or horse In the tissue of family name's body, also, above-mentioned retained austenite, by applying 2% strain the retained austenite of martensite is mutually changed into Ratio is 20～50%.

In addition, Patent Document 2 discloses the excellent high-strength steel sheet of a kind of elongation and hole expandability, its feature exists In with containing C in terms of quality %：More than 0.05% and less than 0.35%, Si：More than 0.05% and less than 2.00%, Mn： More than 0.8% and less than 3.0%, P：More than 0.0010% and less than 0.1000%, S：More than 0.0005% and 0.0500% with Under, Al：More than 0.01% and less than 2.00% and surplus be made up of the steel that Fe and inevitable impurity are constituted, metal structure It is described using ferrite or bainite or tempered martensite as main body and containing more than 3% and less than 30% retained austenite In steel plate, in the boundary that above-mentioned austenite connects with ferrite, bainite and martensite, the center in above-mentioned austenite is dense Concentration C gb of the crystal boundary of degree Cgc and austenite crystal meet the austenite crystal in the range of Cgb/Cgc ＞ 1.3 be 50% with On.

Patent Document 3 discloses a kind of high-strength steel sheet, it is characterised in that contain C in terms of quality %：Exceed 0.17% and less than 0.73%, Si：Less than 3.0%, Mn：More than 0.5% and less than 3.0%, P：Less than 0.1%, S：0.07% Below, Al：Less than 3.0% and N：Less than 0.010%, and meet Si+Al：More than 0.7%, surplus is by Fe and inevitably Impurity is constituted, and used as steel plate tissue, it is more than 10% and less than 90% that martensitic phase organizes the area occupation ratio of entirety for steel plate, residual The amount of remaining austenite is that the bainite ferrite in more than 5% and less than 50%, top bainite is overall relative to steel plate tissue Area occupation ratio be more than 5%, in above-mentioned martensite more than 25% be tempered martensite, above-mentioned martensitic phase for steel plate organize it is whole Bainite ferrite in the area occupation ratio of body, the amount of above-mentioned retained austenite and above-mentioned top bainite organizes whole relative to steel plate The area occupation ratio of body adds up to more than 65%, polygonal ferrite relative to steel plate organize overall area occupation ratio meet 10% with Under, and the average C amounts in above-mentioned retained austenite are more than 0.70%, the TS of the steel plate is more than 980MPa.

Patent Document 4 discloses the yield-ratio high-strength cold-rolled steel sheet that a kind of TS is more than 980MPa, its feature It is, with containing C in terms of quality %：More than 0.06% and less than 0.24%, Si：Less than 0.3%, Mn：More than 0.5% and Less than 2.0%, P：Less than 0.06%, S：Less than 0.005%, Al：Less than 0.06%, N：Less than 0.006%, Mo：0.05% with Upper and less than 0.50%, Ti：More than 0.03% and less than 0.20%, V：More than 0.15 and less than 1.20%, surplus is by Fe and not Evitable impurity composition, C, Ti, Mo, V content meet 0.8≤(C/12)/{ (Ti/48)+(Mo/96)+(V/51) }≤1.5 Into being grouped into, ferrite is calculated as more than 95% with area ratio, carbide containing Ti, Mo and V of the average grain diameter less than 10nm Being dispersed to precipitate, also, be somebody's turn to do the carbide containing Ti, Mo and V, there is Ti, Mo, V for being represented by atom % to meet V/ (Ti+Mo+V) >=0.3 average composition.

Patent Document 5 discloses a kind of high-strength steel sheet of excellent processability, it is characterised in that with quality % Meter contains C：More than 0.05% and less than 0.30%, Si：More than 0.01% and less than 2.50%, Mn：More than 0.5% and 3.5% Below, P：More than 0.003% and less than 0.100%, S：Less than 0.02%, Al：More than 0.010% and less than 1.500%, Si+ Al：More than 0.5% and less than 3.0%, surplus be made up of Fe and inevitable impurity into being grouped into, with terms of area occupation ratio The martensite of the tempered martensite containing more than 20% ferrite, more than 10% and less than 60%, more than 0% and 10%, with It is hard with ferritic Vickers that volume fraction meter contains more than 3% and 10% retained austenite, the Vickers hardness (m) of tempered martensite The ratio m/f of degree (f) is less than 3.0 metal structure.

Patent Document 6 discloses the material in a kind of steel band fluctuation it is little have excellent moldability it is high-strength hot-dip zinc-coated Steel band, it is characterised in that with containing C in terms of quality %：More than 0.05% and less than 0.2%, Si：More than 0.5% and 2.5% Below, Mn：More than 1.5% and less than 3.0%, P：More than 0.001% and less than 0.05%, S：More than 0.0001% and 0.01% Below, Al：More than 0.001% and less than 0.1%, N：More than 0.0005% and less than 0.01%, surplus by Fe and inevitable Impurity constitute into being grouped into, with containing the shared face in tissue entirety of ferrite and martensite, above-mentioned ferritic phase Product rate is more than 50%, the microscopic structure that the area occupation ratio of above-mentioned martensite is more than 30% and less than 50%, and, in steel band The difference of ultimate tensile strength and minimum tensile strength is below 60MPa.

Prior art literature

Patent document

Patent document 1：Japanese Unexamined Patent Publication 2004-218025 publications

Patent document 2：Japanese Unexamined Patent Publication 2011-195956 publications

Patent document 3：Japanese Unexamined Patent Publication 2010-90475 publications

Patent document 4：Japanese Unexamined Patent Publication 2008-174802 publications

Patent document 5：Japanese Unexamined Patent Publication 2010-275627 publications

Patent document 6：Japanese Unexamined Patent Publication 2011-32549 publications

The content of the invention

Invent problem to be solved

But, in the high-strength steel sheet described in patent document 1, disclose processability and shape freezing be excellent, patent In high-strength steel sheet described in document 2, disclose elongation and hole expandability is excellent, the high intensity described in patent document 3 In steel plate, disclose in processability, particularly ductility and stretch flangeability it is excellent, but do not account for stable material quality, i.e. The fluctuation of TS.

In yield-ratio high-strength cold-rolled steel sheet described in patent document 4, used costliness elements Mo, V, therefore into This height.Additionally, the elongation (EL) as little as about 19% of the steel plate.

In high-strength steel sheet described in patent document 5, for example, show that TS × EL is for about under the TS of more than 980MPa 24000MPa%, it is higher than versatile material, but in terms of the nearest requirement for steel plate is tackled, the elongation (EL) of steel plate is still It is insufficient.

In high-strength hot-dip zinc-coated steel band described in patent document 6, the fluctuation that discloses material in steel band is little, formability It is excellent, but retained austenite is not applied flexibly, therefore remain the low problems of EL.

The present invention is in view of above-mentioned present situation, its object is to provide while tensile strength (TS) with more than 780MPa Not only ductility is excellent but also stretch flangeability is also excellent and stable material quality is also excellent high-strength steel sheet and its manufacture Method.

It should be noted that in the present invention, stable material quality is excellent to be referred to, the annealing temperature change 40 in annealing The variation of TS when DEG C (± 20 DEG C) is that Δ TS is below 40MPa (preferably below 36MPa) and annealing temperature change 40 DEG C when EL variation be Δ EL be less than 3% (preferably less than 2.4%) situation.

For the method for solve problem

Inventor solves the above problems and further investigation has been repeated, and is as a result found that following item.

After heating steel billet to predetermined temperature, implement hot rolling and obtain hot rolled plate, as needed after hot rolling to hot rolled plate Implement heat treatment, makes hot rolled plate softening.Then, after by the first time annealing in the austenite one phase area after cold rolling Cooling velocity controls to suppress ferrite transformation and pearlitic transformation.

Then, by making second annealing before organize the formation of martensite single phase structure, bainite homogeneous structure or with Martensite and bainite as main body tissue, cooling after annealing at second and to generate substantial amounts of during keeping be not many The ferrite and bainite ferrite of side shape.

It is not that polygonal ferrite and bainite ferrite are generated in a large number by making this, it can be ensured that fine remnants are difficult to understand The appropriate amount of family name's body.Therefore, using ferrite and bainite ferrite as main body, the group comprising fine retained austenite is formed Knit, the TS with more than 780MPa can be manufactured, not only ductility is excellent but also stretch flangeability is excellent and stable material quality The manufacture of the excellent high-strength steel sheet of property.

The present invention is completed based on above-mentioned opinion.

I.e., purport of the invention constitutes as described below.

1. a kind of high-strength steel sheet, it is characterised in that

With as follows into being grouped into：Contain C in terms of quality %：More than 0.08% and less than 0.35%, Si：More than 0.50% And less than 2.50%, Mn：More than 1.60% and less than 3.00%, P：More than 0.001% and less than 0.100%, S：0.0001% Above and less than 0.0200% and N：More than 0.0005% and less than 0.0100%, surplus is by Fe and inevitable impurity structure Into,

And with following structure of steel：

In terms of area occupation ratio, ferrite and bainite ferrite add up to more than 25% and less than 80%, martensite is 3% Above and less than 20%, in terms of volume fraction, retained austenite is more than 10%,

The average crystallite particle diameter of above-mentioned retained austenite is less than 2 μm,

Average Mn amounts (quality %) in above-mentioned retained austenite is more than 1.2 times of Mn amounts (quality %) in steel,

And the face of the retained austenite of more than 2.1 times with C amounts (quality %) in steel of average C amounts (quality %) Product rate is more than the 60% of the area occupation ratio of whole retained austenites.

2. the high-strength steel sheet as described in above-mentioned 1, it is characterised in that mentioned component composition is further contained in terms of quality % Selected from Al：More than 0.01% and less than 1.00%, Ti：More than 0.005% and less than 0.100%, Nb：More than 0.005% and Less than 0.100%, Cr：More than 0.05% and less than 1.00%, Cu：More than 0.05% and less than 1.00%, Sb：More than 0.0020 And less than 0.2000%, Sn：More than 0.0020% and less than 0.2000%, Ta：More than 0.0010% and less than 0.1000%, Ca：More than 0.0003% and less than 0.0050%, Mg：More than 0.0003% and less than 0.0050% and REM：More than 0.0003% And at least one element in less than 0.0050%.

3. a kind of manufacture method of high-strength steel sheet, it is characterised in that

By with described in above-mentioned 1 or 2 into the heating steel billet being grouped into more than 1100 DEG C and less than 1300 DEG C,

Finish rolling outlet side temperature is set as into that more than 800 DEG C and less than 1000 DEG C form to carry out hot rolling to above-mentioned steel billet Steel plate,

Average coiling temperature is set as more than 450 DEG C and less than 700 DEG C to batch above-mentioned steel plate,

Pickling processes are implemented to above-mentioned steel plate,

Then, arbitrarily by above-mentioned steel plate more than 450 DEG C and Ac₁At temperature below transformation temperature keep more than 900s and The time of below 36000s,

Then, above-mentioned steel plate is carried out with more than 30% reduction ratio it is cold rolling,

Then, enter to be about to the first time annealing that above-mentioned steel plate is heated to more than 820 DEG C and less than 950 DEG C of temperature,

Then, above-mentioned steel plate is cooled to below Ms points with the average cooling rate to 500 DEG C of 15 DEG C/more than s First cooling stop temperature,

Then, enter to be about to above-mentioned steel plate to be again heated at more than 740 DEG C and second annealing of less than 840 DEG C of temperature Reason,

Then, above-mentioned steel plate is cooled to into more than 300 DEG C with the average cooling rate of 10 DEG C/more than s and 50 DEG C/below s And the temperature of less than 550 DEG C of the second cooling stopping temperature range,

Above-mentioned steel plate is stopped into the time of holding more than 10s in temperature range in the above-mentioned second cooling,

So as to manufacture the high-strength steel sheet described in above-mentioned 1 or 2.

4. the manufacture method of the high-strength steel sheet as described in above-mentioned 3, it is characterised in that stop temperature in the above-mentioned second cooling In the range of keep after, further enter to be about to above-mentioned steel plate and be heated to the third time of more than 100 DEG C and less than 300 DEG C of temperature to anneal Process.

5. a kind of manufacture method of high strength galvanized steel plate, it is characterised in that to the high-strength steel sheet described in above-mentioned 1 or 2 Implement zinc-plated process.

Invention effect

In accordance with the invention it is possible to effectively obtain the TS with more than 780MPa, not only ductility is excellent but also extends convex The high-strength steel sheet that edge is also excellent and stable material quality is excellent.In addition, by the height that will be obtained according to the method for the present invention Strength steel sheet is applied in such as automotive structural members, can realize that the fuel efficiency that body lightening is brought improves, industry On value it is very big.

Specific embodiment

Hereinafter, an embodiment of the invention is specifically illustrated.

In the present invention, by heating steel billet to predetermined temperature after, hot rolling is carried out to the steel billet and hot rolled plate is obtained, then, root According to needing after hot rolling to hot rolled plate implement heat treatment, hot rolled plate softening is made.Then, by the austenite one phase after cold rolling Carry out cooling velocity control to suppress ferrite transformation and pearlitic transformation after the first time annealing in area, make second annealing Front organizes the formation of martensite single phase structure, bainite homogeneous structure or using martensite and bainite as the tissue of main body. By forming such tissue, in the cooling after second annealing and process can be kept to generate substantial amounts of ferrite and bainite Ferrite, and then it is able to ensure that the appropriate amount of fine retained austenite.It is such with ferrite and bainite ferrite The steel plate of the tissue as main body and comprising fine retained austenite is the tensile strength (TS) with more than 780MPa, not only The high-strength steel sheet that ductility is excellent and stretch flangeability is also excellent and stable material quality is also excellent.

It should be noted that in the present invention, be only called as above-mentioned ferrite it is ferritic in the case of, with needle-like Ferrite is used as main body, but it is also possible to containing polygonal ferrite, non-recrystallization ferrite.But, in order to ensure good prolongs Malleability, preferably by non-recrystallization ferrite to be suppressed to less than 5% based on above-mentioned ferritic area occupation ratio.

First, the steel in the present invention is shown in into the proper range and its restriction reason being grouped into as follows.

C：More than 0.08 mass % and below 0.35 mass %

C is the element important when steel is strengthened, with high solution strengthening ability.Using the tissue based on martensite It is the requisite element for adjusting the area occupation ratio of martensite, hardness in situation of reinforcing etc..

Here, when C amounts are less than 0.08 mass %, it is impossible to which the area occupation ratio of the martensite needed for obtaining, martensite will not hard Change, therefore, cannot get the sufficient intensity of steel plate.On the other hand, C amount more than 0.35 mass % when, can produce steel plate embrittlement, The worry of delayed fracture.

Therefore, C amount be set as more than 0.08 mass % and below 0.35 mass %, it is more than preferably 0.12 mass % and Scope below 0.30 mass %, more than more preferably 0.17 mass % and below 0.26 mass %.

Si：More than 0.50 mass % and below 2.50 mass %

Si is to suppress the effective element of generation of carbide for retained austenite is decomposed.Additionally, Si is in ferrite In there is high solution strengthening ability, and with make solid solution C from ferrite be expelled to austenite and by ferrite it is purifying, from And improve the property of the ductility of steel plate.In addition, the Si being solid-solution in ferrite has and improving work hardening capacity, improving iron element The effect of the ductility of body itself.In addition, the fluctuation of the fluctuation of TS, EL can be reduced.In order to obtain such effect, need to contain There are Si amounts more than 0.50 mass %.

On the other hand, when Si amounts are more than 2.50 mass %, abnormal structure is flourishing, and the ductility of steel plate and stable material quality drop It is low.Therefore, Si amounts are set as more than 0.50 mass % and below 2.50 mass %, more than preferably 0.80 mass % and 2.00 matter Amount below %, more than more preferably 1.20 mass % and below 1.80 mass %.

Mn：More than 1.60 mass % and below 3.00 mass %

Mn is effective for the intensity for guaranteeing steel plate.In addition, quenching degree can be improved and make complex tissue become easy. Meanwhile, Mn has pearlite, the effect of the generation of bainite suppressed in cooling procedure, makes the phase transformation from austenite to martensite Become easy.In order to obtain such effect, need to make Mn amounts for more than 1.60 mass %.

On the other hand, when Mn amounts are more than 3.00 mass %, the Mn segregations in thickness of slab direction become notable, cause stable material quality Reduction.Therefore, Mn is measured and is set as more than 1.60 mass % and below 3.00 mass %, more than preferably 1.60 mass % and low More than 2.5 mass %, more preferably 1.80 mass % and below 2.40 mass %.

P：More than 0.001 mass % and below 0.100 mass %

P is the effect with solution strengthening, the element that can be added according to desired intensity.In addition, being for promoting Enter ferrite transformation and to complex tissueization also effective element.In order to obtain such effect, need to make P amounts be 0.001 matter Amount more than %.

On the other hand, when P amounts are more than 0.100 mass %, the deterioration of weldability can be caused, also, zinc coating is being carried out In the case of Alloying Treatment, reduce alloying speed and damage the quality of zinc coating.Therefore, P amounts are set as 0.001 matter Below amount more than % and 0.100 mass %, more than preferably 0.005 mass % and below 0.050 mass %.

S：More than 0.0001 mass % and below 0.0200 mass %

S makes steel brittle in cyrystal boundary segregation in hot-working, and local deformation is enable in the form of sulfide Power is reduced.Therefore, content needs to be set as below 0.0200 mass % in steel.

On the other hand, the restriction from production technology considers, needs to make S amounts be more than 0.0001 mass %.Therefore, S amounts It is set as more than 0.0001 mass % and below 0.0200 mass %, more than preferably 0.0001 mass % and 0.0050 mass % Below.

N：More than 0.0005 mass % and below 0.0100 mass %

N is the element for deteriorating the ageing resistance of steel.Particularly, N amount more than 0.0100 mass % when, ageing resistance it is bad Change becomes notable, therefore, its amount is more few more preferred.

On the other hand, the restriction from production technology considers that N amounts need to be set as more than 0.0005 mass %.Therefore, N Amount is set as more than 0.0005 mass % and below 0.0100 mass %, more than preferably 0.0005 mass % and 0.0070 matter Amount below %.

The high-strength steel sheet of the present invention preferably further contains alone or in combination above-mentioned on the basis of being grouped into Selected from Al：More than 0.01 mass % and below 1.00 mass %, Ti：More than 0.005 mass % and below 0.100 mass %, Nb： More than 0.005 mass % and below 0.100 mass %, Cr：More than 0.05 mass % and below 1.00 mass %, Cu：0.05 matter Amount more than % and 1.00 mass % below, Sb：More than 0.0020 mass % and below 0.2000 mass %, Sn：0.0020 matter Amount more than % and 0.2000 mass % below, Ta：More than 0.0010 mass % and below 0.1000 mass %, Ca：0.0003 matter Amount more than % and 0.0050 mass % below, Mg：More than 0.0003 mass % and below 0.0050 mass %, REM：0.0003 matter At least one element in below amount more than % and 0.0050 mass %.It should be noted that steel plate into the surplus being grouped into For Fe and inevitable impurity.

Al：More than 0.01 mass % and below 1.00 mass %

Al is to generate ferrite, the effective element of balance to improving intensity and ductility.In order to obtain such effect, Need to make Al amounts for more than 0.01 mass %.

On the other hand, when Al amounts are more than 1.00 mass %, the deterioration of surface texture is caused.Therefore, Al amounts are preferably 0.01 More than quality % and below 1.00 mass %, more than more preferably 0.03 mass % and below 0.50 mass %.

Ti and Nb forms fine precipitate and raises intensity in hot rolling or when annealing.In order to obtain such effect Really, Ti amounts and Nb amounts need to add respectively more than 0.005 mass %.On the other hand, Ti amounts and Nb are measured respectively more than 0.100 matter During amount %, formability is reduced.Therefore, addition Ti and Nb in the case of, its content be respectively set as more than 0.005 mass % and Below 0.100 mass %.

Cr and Cu serve not only as solution strengthening element and play a role, and in the cooling procedure in annealing that austenite is steady Fixedization, makes complex tissue become easy.In order to obtain such effect, Cr amounts and Cu amounts need to be respectively set as 0.05 matter Amount more than %.

On the other hand, when Cr amounts, Cu amounts are more than 1.00 mass %, the formability of steel plate is reduced.Therefore, in addition Cr and Cu In the case of, its content is respectively set as more than 0.05 mass % and below 1.00 mass %.

The decarburization in the region of about tens of μm of the steel plate top layer produced from the nitridation, oxidation that suppress due to surface of steel plate Viewpoint consideration, is added as needed on Sb and Sn.This is because, when suppressing such nitridation, oxidation, prevent the geneva of surface of steel plate The growing amount of body is reduced, effective for the intensity, the stable material quality that guarantee steel plate.On the other hand, with regard to these elements, exceed 0.2000 mass % and when being excessively added, cause the reduction of toughness.Therefore, in the case of addition Sb and Sn, its content difference It is set as in the scope more than 0.0020 mass % and below 0.2000 mass %.

Ta in the same manner as Ti, Nb, generate alloy carbide, alloy carbonitride and contribute to high intensity.Additionally, one Divide and be solid-solution in Nb carbide, Nb carbonitrides, generate miscible precipitate as (Nb, Ta) (C, N), significantly inhibit precipitate Coarsening.Additionally, it is believed that the suppression of the coarsening of precipitate has the stabilized effect of contribution rate for improving the intensity to steel plate Really.It is therefore preferable that containing Ta.

Here, the stabilized effect of aforesaid precipitate more than 0.0010 mass % is obtained by making the content of Ta, On the other hand, even if Ta is excessively added, precipitate stabilization effect also saturation, and also cost of alloy increases.Therefore, in addition Ta In the case of, its content is set as in the scope more than 0.0010 mass % and below 0.1000 mass %.

Ca, Mg and REM are the elements for deoxidation.In addition, being for making the Form Sphere of sulfide, improving sulfide To local ductility and the effective element of the adverse effect of stretch flangeability.In order to obtain these effects, need to add respectively It is more than 0.0003 mass %.On the other hand, when Ca, Mg and REM are excessively added more than 0.0050 mass %, field trash can be caused Deng increase and on surface, internal produce defect etc..

Therefore, addition Ca, Mg and REM in the case of, its content be respectively set as more than 0.0003 mass % and Below 0.0050 mass %.

Then, microscopic structure is illustrated.

Ferrite is total with the area occupation ratio of bainite ferrite：More than 25% and less than 80%

The high-strength steel sheet of the present invention is included in main as in the tissue of main body using the malleable soft ferrite of richness It is dispersed with the complex tissue undertaken the retained austenite of ductility He undertake the martensite of intensity.And, in order to ensure abundant Ductility and stretch flangeability, in the present invention, need to make adding up to for ferrite and the area occupation ratio of bainite ferrite More than 25%.On the other hand, in order to ensure intensity, need to make the area occupation ratio of ferrite and bainite ferrite to add up to 80% Below.

Bainite ferrite in the present invention is after the annealing more than 740 DEG C and within the scope of less than 840 DEG C of temperature The ferrite generated during less than 600 DEG C of cooling and holding, is the iron higher than dislocation density with common ferritic phase Ferritic.

In addition, " area occupation ratio of ferrite and bainite ferrite " is obtained by following method.First, pair with steel plate After the parallel thickness of slab section of rolling direction (L sections) is ground, corroded with 3 volume % nitals, (swept using SEM Retouch electron microscope) with 2000 times of multiplying power to the position of thickness of slab 1/4 (in the depth direction equivalent to thickness of slab from surface of steel plate 1/4 position) 10 visuals field of observation.Then, using resulting organization chart picture, using Media Cybernetics companies Image-Pro, calculates the area occupation ratio of each tissue (ferrite, bainite ferrite) in 10 visuals field.By above-mentioned 10 visuals field Area occupation ratio is averagely set as " area occupation ratio of ferrite and bainite ferrite ".It should be noted that above-mentioned organization chart picture In, ferrite and bainite ferrite are presented the tissue (substrate microstructure) of grey, and retained austenite and martensite are presented white Tissue.

Additionally, the EBSD (EBSD method) that is identified by of ferrite and bainite ferrite determines to carry out. The crystal grain (phase) of the sub boundary comprising grain misorientation less than 15 ° is judged as into bainite ferrite, its area occupation ratio is obtained, as shellfish The ferritic area occupation ratio of family name's body.Ferritic area occupation ratio deducts bainite iron element in the area occupation ratio by the tissue from above-mentioned grey The area occupation ratio of body and calculate.

The area occupation ratio of martensite：More than 3% and less than 20%

In the present invention, in order to ensure the intensity of steel plate, the area occupation ratio for needing to make martensite is more than 3%.On the other hand, In order to ensure the good ductility of steel plate, the area occupation ratio for needing to make martensite is less than 20%.In addition, in order to ensure better Ductility and stretch flangeability, the area occupation ratio of preferred martensite is less than 15%.

It should be noted that " area occupation ratio of martensite " is obtained by following method.First, the L sections of steel plate are entered Row grinding after, with 3 volume % nitals corrode, using SEM with 2000 times of multiplying power to the position of thickness of slab 1/4 (from steel plate Surface rise in the depth direction equivalent to thickness of slab 1/4 position) observation 10 visuals field.Then, using resulting organization chart Picture, using above-mentioned Image-Pro, calculates the white martensite in 10 visuals field and total area occupation ratio of retained austenite.So Afterwards, the area occupation ratio of retained austenite is deducted from the mean value of these values, thus, it is possible to obtain " area occupation ratio of martensite ".Separately Outward, in above-mentioned organization chart picture, martensite and retained austenite are presented white tissue.Here, the area occupation ratio of retained austenite Value using retained austenite as follows volume fraction value.

The volume fraction of retained austenite：More than 10%

In the present invention, in order to ensure good ductility and intensity and the balance of ductility, need to make retained austenite Volume fraction be more than 10%.In order to ensure better ductility and intensity and the balance of ductility, preferred retained austenite Volume fraction be more than 12%.

In addition, with regard to the volume fraction of retained austenite, steel plate is ground to into 1/4 face in thickness of slab direction, by the thickness of slab 1/4 The diffracting X-rays intensity in face is obtained.Incident X-rays use MoK alpha rays, obtain retained austenite { 111 }, { 200 }, { 220 }, the integrated intensity at the peak in { 311 } face is relative to ferritic { 110 }, { 200 }, the integrated intensity at the peak in { 211 } face The strength ratios of 12 kinds of whole combinations, using their mean value as retained austenite volume fraction.

The average crystallite particle diameter of retained austenite：Less than 2 μm

The miniaturization of the crystal grain of retained austenite contributes to the ductility of steel plate and the raising of stable material quality.Therefore, it is Guarantee good ductility and stable material quality, the average crystallite particle diameter for needing to make retained austenite is less than 2 μm.In order to true Better ductility and stable material quality is protected, the average crystallite particle diameter for preferably making retained austenite is less than 1.5 μm.

It should be noted that in the present invention, " average crystallite particle diameter of retained austenite " is obtained by following method. First, using TEM (transmission electron microscope), 20 visuals field are observed with 15000 times of multiplying power, obtains organization chart picture.Using upper Image-Pro is stated, the area of each retained austenite crystal grain in the organization chart picture in 20 visuals field is obtained, round equivalent is calculated straight These values are carried out averagely, obtaining " average crystallite particle diameter of retained austenite " by footpath.Here, the above-mentioned visual field is observed so that thickness of slab 1/4 part is ground for the mode at thickness of slab center from the table back side so as to which thickness is 0.3mm, then, from the table back side electricity is carried out Solution grinding, perforate, the part relatively thin for the thickness of slab around the hole is observed using TEM from plate face direction.

Average Mn amounts (quality %) in retained austenite is more than 1.2 times of Mn amounts (quality %) in steel

It is in the present invention extremely important controlling elements.

This is because, Mn's amounts (quality %) average Mn amounts (quality %) in retained austenite being set as in steel More than 1.2 times, and make martensite single phase structure, bainite homogeneous structure to be organized the formation of before second annealing or is mixed to deposit In the tissue for having martensite and bainite, thus, in the temperature-rise period of second annealing, first, the carbide of Mn is enriched with Separate out.Then, the carbide becomes the core based on the austenite of reverse transformation, and finally giving dispersed has fine residual austenite The tissue of body, stable material quality is improved.

It should be noted that being analyzed by using FE-EPMA (field emission electron probe-microanalyser), calculate each Average Mn amounts (quality %) of phase.

In addition, average Mn amounts (quality %) in retained austenite as long as the Mn amounts 1.2 times of (quality %) in steel with On then the upper limit be not particularly limited, preferably from about 2.5 times.

The area occupation ratio of the retained austenite of more than 2.1 times with C amounts (quality %) in steel of average C amounts (quality %) For more than the 60% of the area occupation ratio of whole retained austenites

In order to by assuring that the volume fraction of desired stable retained austenite needs to make tool guaranteeing good ductility The area occupation ratio for having the retained austenite of more than 2.1 times of C amounts (quality %) in steel of average C amounts (quality %) is all remaining More than the 60% of the area occupation ratio of austenite.

It should be noted that the condition cannot be realized after once making annealing treatment, obtained first by twice annealing process.

In addition, the retained austenite of more than 2.1 times with C amounts (quality %) in steel of average C amounts (quality %) The upper limit of area occupation ratio is not particularly limited, and preferably from about 95%.

In the present invention, there is bayesian body phase in processing in the cooling later stage and austempering after making annealing treatment at second Become.By there is the phase transformation, bainite ferrite on the minor axis direction of the austenite after spiculation breaks austenite Open, generate the fine retained austenite that average crystallite particle diameter is less than 2 μm.And, the residual austenite generated by the process More than 2.1 times of C amounts (quality %) in average C amounts (quality %) the up to steel of body, it can be ensured that extremely good ductility.

Here, value of the value of the area occupation ratio of retained austenite using the volume fraction of above-mentioned retained austenite.Need explanation , in the present invention, it is analyzed by using FE-EPMA (field emission electron probe-microanalyser), calculate each phase Average Mn amounts (quality %) and average C amounts (quality %).

In addition, in the microscopic structure of the present invention, except ferrite, bainite ferrite, martensite and retained austenite with Outward, can also containing the carbide such as tempered martensite, pearlite, cementite, as the tissue of other steel plates known tissue. It should be noted that when its hetero-organization such as these tempered martensites is calculated as less than 10% scope with area occupation ratio, even if containing Without compromising on the effect of the present invention.

Then, manufacture method is illustrated.

With regard to the high-strength steel sheet of the present invention, by with above-mentioned predetermined into the heating steel billet being grouped into more than 1100 DEG C And less than 1300 DEG C, finish rolling outlet side temperature is set as more than 800 DEG C and less than 1000 DEG C to carry out hot rolling, make steel plate.

Then, average coiling temperature is set as more than 450 DEG C and less than 700 DEG C to batch steel plate, to steel plate Implement pickling processes, then, arbitrarily by steel plate more than 450 DEG C and Ac₁More than 900s is kept at temperature below transformation temperature And the time of below 36000s.Then, steel plate is carried out with more than 30% reduction ratio cold rolling, carries out being heated to more than 820 DEG C And the first time annealing of less than 950 DEG C of temperature.

Then, above-mentioned steel plate is cooled to below Ms points with the average cooling rate to 500 DEG C of 15 DEG C/more than s First cooling stop temperature.Then, enter to be about to second that steel plate is again heated to more than 740 DEG C and less than 840 DEG C of temperature Annealing.Then, by steel plate with the average cooling rate of 10 DEG C/more than s and 50 DEG C/below s be cooled to more than 300 DEG C and Less than 550 DEG C of the second cooling stops temperature range, stops keeping more than 10s in the temperature of temperature range in second cooling.

Further, in the present invention, as described later, it is also possible to after the above-mentioned second cooling stops being kept in temperature range, enter The third time annealing that above-mentioned steel plate is heated to more than 100 DEG C and less than 300 DEG C of temperature is about in one stepping.

In addition, the high strength galvanized steel plate of the present invention can be by implementing public plating to above-mentioned high-strength steel sheet Zinc processes to manufacture.

The heating-up temperature of steel billet：More than 1100 DEG C and less than 1300 DEG C

Precipitate present in the heating period of steel billet is deposited in the steel plate for finally giving in the form of thick precipitate Intensity is not being contributed, accordingly, it would be desirable to Ti, Nb system precipitate re-dissolved separated out when making casting.

Here, when the heating-up temperature of steel billet is less than 1100 DEG C, the abundant dissolving of carbide is difficult, is produced because rolling is carried The problems such as dangerous increase that failure during the hot rolling that the increase of lotus causes occurs.In addition, in addition it is also necessary to by the bubble on steel billet top layer, partially The defects such as analysis are wiped off, the crackle, concavo-convex of surface of steel plate are reduced, so as to realize smooth surface of steel plate.Therefore, steel billet of the invention Heating-up temperature need to be set as more than 1100 DEG C.On the other hand, when the heating-up temperature of steel billet is more than 1300 DEG C, oxide skin loss Increase with the increase of amount of oxidation.Therefore, the heating-up temperature of steel billet needs to be set as less than 1300 DEG C.Therefore, steel billet plus Hot temperature is set as more than 1100 DEG C and less than 1300 DEG C.Preferably more than 1150 DEG C and less than 1250 DEG C.

In order to prevent gross segregation, steel billet from preferably manufacturing by continuous metal cast process, but it is also possible to cast by ingot casting method, sheet billet Make method etc. to manufacture.In addition, in the present invention it is possible to using showing for manufacturing after steel billet, be first cooled to room temperature and then heat again There is method.In addition it is also possible to have no problem application be not cooled to room temperature and be encased in heating furnace with the state of warm piece or Somewhat carry out directly being carried out after thermal protection the energy saving techniques such as roll etc., direct sending rolling/Direct Rolling.In addition, by steel billet usual Under conditions of laminated base using roughing, but in the case where making heating-up temperature relatively low, the sight of failure when hot rolling is prevented Point is considered, preferably before finish rolling sheet billet is heated using strip heater etc..

The finish rolling outlet side temperature of hot rolling：More than 800 DEG C and less than 1000 DEG C

Steel billet after heating is carried out into hot rolling by roughing and finish rolling and hot rolled steel plate is formed.Now, finish rolling outlet side temperature When degree is more than 1000 DEG C, the growing amount of oxide (oxide skin) is sharply increased, and base steel is thicker with the interface of oxide, pickling, cold Surface quality after rolling has the tendency of deterioration.In addition, after pickling, in residual for locally lying in hot rolling oxide skin etc., to prolonging Malleability, stretch flangeability have a negative impact.Additionally, crystallization particle diameter become over it is thick, sometimes plus man-hour produce punching press Product rough surface.

On the other hand, finish rolling outlet side temperature is less than 800 DEG C, and rolling loads increase, rolling load increases.In addition, Ovshinsky Reduction ratio of the body under non-recrystallization state is uprised, and abnormal texture is flourishing, and the intra-face anisotropy in end article becomes aobvious Write.As a result, can not only damage the uniformity of material, stable material quality, ductility itself is also reduced.

Accordingly, it would be desirable to the finish rolling outlet side temperature of hot rolling is set as into the scope of more than 800 DEG C and less than 1000 DEG C.It is preferred that It is set as the scope of more than 820 DEG C and less than 950 DEG C.

Average coiling temperature after hot rolling：More than 450 DEG C and less than 700 DEG C

When the average coiling temperature of the steel plate after hot rolling is more than 700 DEG C, the ferritic crystallization particle diameter of hot rolled plate tissue increases Greatly, it is difficult to guarantee the desired intensity of final annealing plate.On the other hand, when the average coiling temperature after hot rolling is less than 450 DEG C, heat Roll plate intensity rising, it is cold rolling in rolling load increase, productivity ratio reduce.

Accordingly, it would be desirable to the average coiling temperature after by hot rolling is set as more than 450 DEG C and less than 700 DEG C.It is preferably set to More than 450 DEG C and less than 650 DEG C.

It should be noted that roughing plate can also be engaged with each other in hot rolling and continuously carry out finish rolling.In addition, first right Roughing plate is batched also, and it doesn't matter.In addition, in order to reduce rolling loads during hot rolling, can be by a part for finish rolling or complete Portion is set as lubrication and rolling.Homogenization from plate profile, from the viewpoint of the homogenization of material, it is also have to be lubricated rolling Effect.It should be noted that coefficient of friction during lubrication and rolling is preferably set to more than 0.10 and less than 0.25 scope.

Pickling is carried out to the hot rolled steel plate of such manufacture.Pickling can remove the oxide of surface of steel plate, therefore, for true It is important to protect the good chemical convertibility of the high-strength steel sheet of end article, coating quality.In addition, pickling can enter Row is once, it is also possible to be divided into repeatedly.

Heat treatment temperature and retention time after the pickling processes of hot rolled plate：More than 450 DEG C and Ac₁Protect below transformation temperature Hold more than 900s and below 36000s

When heat treatment temperature is less than 450 DEG C or the heat treatment retention time is less than 900s, the tempering after the hot rolling of steel plate is not Fully, the uneven tissue for being mixed ferrite, bainite, martensite is formed.And, under the hot rolled plate tissue, The fine uniform structure of steel plate tissue becomes insufficient.As a result, there is following situation：It is thick in the tissue of final annealing plate The ratio of martensite increases, and forms uneven tissue, the hole expandability (stretch flangeability) of final annealing plate and stable material quality Reduce.

On the other hand, when the retention time is heat-treated more than 36000s, productivity ratio is had a negative impact sometimes.Separately Outward, in heat treatment temperature more than Ac₁During transformation temperature, the uneven and hardening of ferrite and martensite or pearlite is formed Thick two-phase structure, in the uneven tissue of cold rolling front formation.As a result, there is following situation：Final annealing plate it is thick The ratio of martensite increase, the hole expandability (stretch flangeability) of final annealing plate and stable material quality are still reduced.

Therefore, the heat treatment temperature after hot rolled plate pickling processes needs to be set as more than 450 DEG C and Ac₁Below transformation temperature, Retention time needs to be set as more than 900s and below 36000s.

Reduction ratio when cold rolling：More than 30%

When reduction ratio is less than 30%, in ensuing annealing, become crystal boundary, the dislocation of the core of reverse transformation to austenite Per unit volume sum reduction, it is difficult to obtain above-mentioned final microscopic structure.Additionally, producing in microscopic structure uneven When, the ductility reduction of steel plate.

Therefore, reduction ratio when cold rolling needs to be set as more than 30%.It is preferably set to more than 40%.Need explanation It is that the number of times, the reduction ratio of each passage with regard to rolling pass is not particularly limited, the effect of the present invention can be obtained.In addition, The upper limit of above-mentioned reduction ratio is not particularly limited, and is industrially practical about 80%.

The temperature for making annealing treatment for the first time：More than 820 DEG C and less than 950 DEG C

When first time annealing temperature is less than 820 DEG C, it is at the heat of two-phase section in ferrite Yu austenite that this is heat-treated to Reason, therefore, ferrite (the polygon iron element generated in the two-phase section in final tissue containing substantial amounts of ferrite with austenite Body).As a result, the fine retained austenite of desired amount will not be generated, it is difficult to guarantee the balance of good intensity and ductility. On the other hand, when first time annealing temperature is more than 950 DEG C, the coarse grains of the austenite in annealing finally will not be generated micro- Thin retained austenite, is still difficult to ensure that the balance of good intensity and ductility, and productivity ratio is reduced.

It should be noted that for the first time the retention time of annealing be not particularly limited, preferably more than 10s and The scope of below 1000s.

The average cooling rate to 500 DEG C after making annealing treatment for the first time：15 DEG C/more than s

It is in the present invention extremely important controlling elements.

When average cooling rate is less than 15 DEG C/s, ferrite and pearlite is generated in cooling, therefore, anneal at second Cannot be using low-temperature phase covert (bainite or martensite) as the tissue of main body in front tissue.As a result, finally will not generate The fine retained austenite of desired amount, accordingly, it is difficult to guarantee the balance of good intensity and ductility.In addition, can also damage The stable material quality of steel plate.It should be noted that the upper limit of above-mentioned average cooling rate is not particularly limited, industrially may The upper limit be about 60 DEG C/s till.

It is cooled to the first cooling below Ms points and stops temperature

In making annealing treatment for the first time, finally it is cooled to the first cooling below Ms points and stops temperature.

Make to organize the formation of martensite single phase structure, bainite homogeneous structure or with geneva before second annealing The tissue of body and bainite as main body.Thus, during the cooling and holding after annealing at second, give birth to below 600 DEG C Into it is grain-boundary shape deformation, be not polygonal ferrite and bainite ferrite and generate in a large number.As a result, being able to ensure that micro- The appropriate amount of thin retained austenite, it can be ensured that good ductility.

The temperature of second annealing：More than 740 DEG C and less than 840 DEG C

When second annealing temperature is less than 740 DEG C, the volume fraction of sufficient austenite, final nothing cannot be guaranteed in annealing Method guarantees the area occupation ratio of desired martensite and the volume fraction of retained austenite.Accordingly, it is difficult to guarantee intensity, and it is difficult to ensure that The balance of good intensity and ductility.On the other hand, when second annealing temperature is more than 840 DEG C, austenite one phase is reached Temperature range, therefore, will not finally generate the fine retained austenite of desired amount.As a result, being still difficult to ensure that good The balance of intensity and ductility.In addition, it is different with the heat treatment of the two-phase section of austenite from ferrite, therefore, hardly There is the caused Mn distribution of diffusion.As a result, average Mn amounts (quality %) in retained austenite is not up to the Mn in steel More than 1.2 times of amount (quality %), it is difficult to guarantee the volume fraction of desired stable retained austenite.It should be noted that the The retention time that double annealing is processed is not particularly limited, preferably more than 10s and below 1000s.

To more than 300 DEG C and less than 550 DEG C second cooling stop temperature range temperature average cooling rate： 10 DEG C/more than s and 50 DEG C/below s

When second makes annealing treatment, to more than 300 DEG C and less than 550 DEG C of the second cooling stopping temperature range temperature Till average cooling rate be less than 10 DEG C/s, substantial amounts of ferrite is generated in cooling, it is difficult to guarantee bainite ferrite and Martensite.Accordingly, it is difficult to guarantee the intensity of steel plate.On the other hand, when average cooling rate is more than 50 DEG C/s, geneva is excessively generated Body, the ductility of steel plate and stretch flangeability are reduced.It should be noted that cooling now is preferably gas cooling, but also may be used Carried out with being applied in combination cold stove, misting cooling, roller cooling, water-cooled etc..

When second cooling of second annealing stops the holding in temperature range (more than 300 DEG C and less than 550 DEG C) Between：More than 10s

When the retention time that above-mentioned second cooling stops in temperature range (more than 300 DEG C and less than 550 DEG C) is less than 10s, Become insufficient to the C enrichments of austenite the carried out time, be finally difficult to ensure that the volume fraction of desired retained austenite.This Outward, it is difficult to make the area of the retained austenite of more than 2.1 times with C amounts (quality %) in steel of average C amounts (quality %) Rate meets more than the 60% of the area occupation ratio of whole retained austenites.On the other hand, when stopping more than 600s, the body of retained austenite Product rate will not increase, and confirmation becomes tendency less than significantly improving for ductility, therefore, although it is not particularly limited, but Preferably below 600s.

Therefore, the retention time that above-mentioned second cooling stops in temperature range is set as more than 10s, preferably 600s with Under.It should be noted that the cooling after keeping can be cooled to desired temperature without the need for special provision by arbitrary method. In addition, above-mentioned desired temperature is preferably room temperature.

The temperature of third time annealing：More than 100 DEG C and less than 300 DEG C

When third time annealing is less than 100 DEG C, the tempering softening of martensite becomes insufficient, it may be difficult to guarantee more Good hole expandability (stretch flangeability).On the other hand, when third time annealing is more than 300 DEG C, retained austenite is decomposed, most It is likely difficult to eventually guarantee the volume fraction of desired retained austenite.Therefore, the temperature for carrying out third time annealing is preferably 100 More than DEG C and less than 300 DEG C.It should be noted that the retention time of third time annealing is not particularly limited, preferably 10s Above and below 36000s.

Implement zinc-plated process

When implementing galvanizing and processing, by the steel plate implemented after above-mentioned annealing be impregnated into more than 440 DEG C and 500 DEG C with Under zinc-plated bath in and implement galvanizing process, then, by airblast etc. adjust coating adhesion amount.Galvanizing is preferably used Al amounts are the zinc-plated bath more than 0.10 mass % and below 0.22 mass %.In addition, when the Alloying Treatment of zinc coating is implemented, After galvanizing is processed, the Alloying Treatment of zinc coating is implemented more than 470 DEG C and within the scope of less than 600 DEG C of temperature.Super Cross when carrying out Alloying Treatment at a temperature of 600 DEG C, there is following situation：Non- transformed austenite is mutually changed into pearlite, it is impossible to really Protect the volume fraction of desired retained austenite, ductility reduction.Therefore, when the Alloying Treatment of zinc coating is carried out, preferably exist Implement the Alloying Treatment of zinc coating within the scope of more than 470 DEG C and less than 600 DEG C of temperature.Furthermore it is possible to implement at electrogalvanizing Reason.

The reduction ratio of the skin-pass after heat treatment is preferably more than 0.1% and less than 1.0% scope.Less than 0.1% When, effect is little, is also difficult to control to, therefore, 0.1% becomes the lower limit of good range.In addition, during more than 1.0%, productivity ratio is notable Reduce, therefore, the upper limit for being set as good range by 1.0%.

Skin-pass can be carried out online, it is also possible to be carried out offline.Furthermore it is possible to disposably carry out the table of target reduction ratio Skin dress rolling, it is also possible to be divided into repeatedly.The condition of other manufacture methods is not particularly limited, from from the viewpoint of productivity ratio, on A series of process such as annealing, galvanizing, the Alloying Treatment of zinc coating stated are preferably in the CGL as hot galvanizing line Carry out in (Continuous Galvanizing Line, continuous hot galvanizing line).After galvanizing, in order to adjust the attachment of coating Amount, can be wiped.It should be noted that the condition of plating beyond above-mentioned condition etc. can be according to the routine side of galvanizing Method.

Embodiment

By with shown in table 1 into being grouped into, surplus is carried out by the steel that Fe and inevitable impurity are constituted using converter Melting, by continuous metal cast process steel billet is made.Resulting steel billet is heated under the conditions shown in Table 2, hot rolling is carried out and is obtained steel Plate.Then, pickling processes are implemented to the steel plate.Then, for No.1～22 shown in table 2,24,25,28,30,31,33,35 ～40,42,44～56, implement hot rolled plate heat treatment to steel plate under the conditions shown in Table 2.For No.31 therein, 33,35 ～40,42,44, implement pickling processes after hot rolled plate heat treatment.

Then, steel plate carried out under the conditions shown in Table 2 it is cold rolling after, under the conditions shown in Table 2 two are implemented to steel plate Secondary or three annealings, obtain high strength cold rolled steel plate (CR).

Further, zinc-plated process is implemented to a part of high strength cold rolled steel plate (CR), obtains hot-dip galvanizing sheet steel (GI), alloying Hot-dip galvanizing sheet steel (GA), plated steel sheet (EG) etc..With regard to galvanizing bath, the zinc of the Al containing 0.19 mass % used in GI Bath, the zinc bath of the Al containing 0.14 mass % used in GA, bath temperature is set as 465 DEG C.Coating adhesion amount is set as every one side 45g/m²(two sides coating), in GA, the Fe concentration in coating is set as more than 9 mass % and below 12 mass %.

It should be noted that Ac₁Transformation temperature (DEG C) is obtained using below equation, and is shown in Table 1.

Ac₁Transformation temperature (DEG C)=751-16 × (%C)+11 × (%Si) -28 × (%Mn) -5.5 × (%Cu)+13 × (%Cr)

Wherein, content (quality %) in the steel of element X (%X) is represented.

In addition, Ms points (DEG C) is obtained using below equation, and it is shown in Table 3.

Ms points (DEG C)=550-361 × (%C) × 0.01 × [the A percentage after the firm annealing of second annealing (%)] -69 × [Mn amounts (%) in retained austenite] -20 × (%Cr) -10 × (%Cu)+30 × (%Al)

Wherein, content (quality %) in the steel of element X (%X) is represented.

With regard to the A percentage (%) after the firm annealing of second annealing described herein, make annealing treatment at second The laggard water-filling quenching (average cooling rate to room temperature of just annealing of (more than 740 DEG C and less than 840 DEG C)：800 DEG C/s with On), it is defined as the area occupation ratio of the martensite of the tissue.It should be noted that the area occupation ratio of martensite can pass through aforesaid side Method is obtaining.

It should be noted that Mn amounts (%) is for the residual of final high-strength steel sheet in the retained austenite in above-mentioned formula Average Mn amounts (quality %) in remaining austenite.

High strength cold rolled steel plate (CR), hot-dip galvanizing sheet steel (GI), alloyed hot-dip galvanized steel sheet (GA) obtained by carrying out, electricity The tension test of galvanized steel plain sheet (EG) etc. and hole expansion test.

In tension test, use so that the mode in the long side of tension test sheet (C directions) vertical with the rolling direction of steel plate JIS5 test film obtained from sample is cut, is carried out according to JIS Z 2241 (2011), determine TS (tensile strength), EL (percentage of total elongation).It should be noted that in the present invention, will be in TS：Under 780MPa levels for EL >=34%, in TS：980MPa levels Down for EL >=27%, in TS：Situation under 1180MPa levels for EL >=23% and TS × EL >=27000MPa% is judged as Well.

Hole expansion test is carried out according to JIS Z 2256 (2010).By resulting each steel plate cut into 100mm × After 100mm, with the hole that 12% ± 1% clearance blanking goes out diameter 10mm, then, using the punch die of internal diameter 75mm with 8ton (7.845kN) in the state of pressing force pressing, the Kong Zhi that crackle produces the limit will in the drift press-in hole of 60 ° of circular cones, be determined Footpath, by following formula limit hole expansibility λ (%) is obtained, and hole expandability is evaluated according to the value of the limit hole expansibility.

Limit hole expansibility λ (%)={ (D_f-D₀)/D₀}×100

Wherein, D_fAperture (mm) when producing for crackle, D₀For initial aperture (mm).It should be noted that in the present invention In, by TS：Under 780MPa levels for λ >=40%, in TS：Under 980MPa levels for λ >=30%, in TS：Under 1180MPa levels for λ >= 20% situation is judged to well.

With regard to stable material quality, in each test example No.1～56, second annealing temperature is set to change ± 20 DEG C to manufacture Same high strength cold rolled steel plate, determines its TS and EL.

It should be noted that in the present invention, when the annealing temperature of second annealing is changed into 40 DEG C (± 20 DEG C) The variation i.e. Δ EL of EL when to be Δ TS change 40 DEG C for below 36MPa, annealing temperature of the variation of TS be less than 2.4% Situation be judged as well.

With regard to the logical plate of hot rolling, the dangerous increase that the failure during hot rolling that will cause because of the increase of rolling loads occurs Situation is judged as bad.

With regard to cold rolling logical plate, by cause because of the increase of rolling loads it is cold rolling when the failure dangerous increase that occurs Situation is judged as bad.

With regard to the surface texture of cold-rolled steel sheet, will be unable to wipe off the defects such as the bubble on steel billet top layer, segregation, surface of steel plate Crackle, concavo-convex increase, the situation of surface of steel plate that cannot smooth be judged as it is bad.In addition, by oxide (oxide skin) Growing amount is sharply increased, the thicker interface of base steel and oxide, pickling, it is cold rolling after surface quality deterioration situation, in pickling Afterwards the situation in the residual for locally lying in hot rolling oxide skin etc. is judged as bad.

With regard to productivity ratio, shape defect, (2) of hot rolled plate are produced to need hot rolling into subsequent processing according to (1) During the shape correction of plate, retention time of (3) annealing it is long when, (4) austempering retention time, (second made annealing treatment Cooling stop temperature range in retention time) it is long when etc. production cycle cost, will not belong to any in (1)～(4) A kind of situation is judged as " height ", the situation for only belonging to (4) is judged as " in ", by belong in (1)～(3) any one Situation is judged as " bad ".

The TS of the high-strength steel sheet of example is more than 780MPa, and ductility and hole expandability (stretch flangeability) are excellent, tool There is the balance of high intensity and ductility, and stable material quality is also excellent.On the other hand, in comparative example, plate, production are led to Any one in balance, the stable material quality of rate, intensity, ductility, hole expandability (stretch flangeability), intensity and ductility with It is upper poor.

Claims

1. a kind of high-strength steel sheet, it is characterised in that

With as follows into being grouped into：Contain C in terms of quality %：More than 0.08% and less than 0.35%, Si：More than 0.50% and Less than 2.50%, Mn：More than 1.60% and less than 3.00%, P：More than 0.001% and less than 0.100%, S：0.0001% with It is upper and less than 0.0200% and N：More than 0.0005% and less than 0.0100%, surplus is made up of Fe and inevitable impurity,

And with following structure of steel：

In terms of area occupation ratio, ferrite and bainite ferrite add up to more than 25% and less than 80%, martensite is more than 3% And less than 20%, in terms of volume fraction, retained austenite is more than 10%,

The average crystallite particle diameter of the retained austenite is less than 2 μm,

Average Mn amounts (quality %) in the retained austenite is more than 1.2 times of Mn amounts (quality %) in steel,

And the area occupation ratio of the retained austenite of more than 2.1 times with C amounts (quality %) in steel of average C amounts (quality %) For more than the 60% of the area occupation ratio of whole retained austenites.

2. high-strength steel sheet as claimed in claim 1, it is characterised in that described further to be contained in terms of quality % into being grouped into Selected from Al：More than 0.01% and less than 1.00%, Ti：More than 0.005% and less than 0.100%, Nb：More than 0.005% and Less than 0.100%, Cr：More than 0.05% and less than 1.00%, Cu：More than 0.05% and less than 1.00%, Sb：More than 0.0020 And less than 0.2000%, Sn：More than 0.0020% and less than 0.2000%, Ta：More than 0.0010% and less than 0.1000%, Ca：More than 0.0003% and less than 0.0050%, Mg：More than 0.0003% and less than 0.0050% and REM：More than 0.0003% And at least one element in less than 0.0050%.

By with described in claim 1 or 2 into the heating steel billet being grouped into more than 1100 DEG C and less than 1300 DEG C,

Finish rolling outlet side temperature is set as into that more than 800 DEG C and less than 1000 DEG C form steel to carry out hot rolling to the steel billet Plate,

Average coiling temperature is set as more than 450 DEG C and less than 700 DEG C to batch the steel plate,

Pickling processes are implemented to the steel plate,

Then, arbitrarily by the steel plate more than 450 DEG C and Ac₁At temperature below transformation temperature keep more than 900s and The time of below 36000s,

Then, the steel plate is carried out with more than 30% reduction ratio it is cold rolling,

Then, enter to be about to the first time annealing that the steel plate is heated to more than 820 DEG C and less than 950 DEG C of temperature,

Then, steel plate is cooled to the average cooling rate to 500 DEG C of 15 DEG C/more than s below Ms points One cooling stops temperature,

Then, enter to be about to second annealing that the steel plate is again heated to more than 740 DEG C and less than 840 DEG C of temperature,

Then, the steel plate is cooled to into more than 300 DEG C and 550 with the average cooling rate of 10 DEG C/more than s and 50 DEG C/below s The second cooling below DEG C stops the temperature of temperature range,

The steel plate is stopped into the time of holding more than 10s in temperature range in the described second cooling,

So as to the high-strength steel sheet described in manufacturing claims 1 or 2.

4. the manufacture method of high-strength steel sheet as claimed in claim 3, it is characterised in that stop temperature in the described second cooling In the range of keep after, further enter to be about to the steel plate and be heated to the third time of more than 100 DEG C and less than 300 DEG C of temperature to anneal Process.

5. a kind of manufacture method of high strength galvanized steel plate, it is characterised in that to the high-strength steel sheet described in claim 1 or 2 Implement zinc-plated process.