CN106460125A - High-strength steel sheet and production method therefor - Google Patents

High-strength steel sheet and production method therefor Download PDF

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Publication number
CN106460125A
CN106460125A CN201580023594.0A CN201580023594A CN106460125A CN 106460125 A CN106460125 A CN 106460125A CN 201580023594 A CN201580023594 A CN 201580023594A CN 106460125 A CN106460125 A CN 106460125A
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less
rolling
steel sheet
strength steel
formability
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CN201580023594.0A
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CN106460125B (en
Inventor
斋藤勇人
小岛克己
多田雅毅
中丸裕树
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0268—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment between cold rolling steps
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

Provided is a high-strength steel sheet that has favorable formability (workability) and strength. Also provided is a production method for the high-strength steel sheet. The high-strength steel sheet is characterized by containing 0.010-0.080 mass% of C, 0.05 mass% or less of Si, 0.10-0.70 mass% of Mn, 0.03 mass% or less of P, 0.020 mass% or less of S, 0.005-0.070 mass% of Al, and 0.0120-0.0180 mass% of N, the remainder having a component composition that comprises Fe and unavoidable impurities, and is characterized in that solid-solution N content is 0.0100 mass% or more as part of the N content, by average ferrite particle diameter being 7.0 micrometer or less, by having a dislocation density of 4.0*1014-2.0*1015 m-2 at a depth of 1/4 sheet thickness from the surface, by having a post-aging tensile strength of 530 MPa or more in the direction perpendicular to the rolling direction, and by having an elongation of 7% or more.

Description

High-strength steel sheet and manufacture method thereof
Technical field
The present invention relates to be suitable for the high-strength steel sheet of the can container material used in the manufacture of food cans, beverage can and Its manufacture method.The high-strength steel sheet of the present invention has particularly excellent formability, easily opens therefore, it is possible to be suitably applied manufacture Capping (EOE), welding tank body.
Background technology
As for manufacturing beverage can, food cans, the main body etc. that is configured to lid, the end, built-up tin steel plate for tanks, sometimes Use is referred to as the steel plate of DR (Double Reduced, secondary cold-rolling) material.DR material carries out cold rolling again after referring to annealing And the steel plate manufacturing.As compared to SR (Single Reduced, the once cold rolling) material only carrying out the little temper rolling of rolling rate, DR material easily can make thickness of slab thinning while hardening.
In recent years, from reducing carrying capacity of environment and cutting down from the viewpoint of cost, seek to cut down for beverage can, food cans The usage amount of steel plate.Therefore, the expectation that easy for the thin-walled property of steel plate DR material is used as steel plate for tanks is increasing.
But, DR material hardening because of processing hardening, therefore, general formability is low, in order to make DR material be suitable as Steel plate for tanks, needs to improve the formability of DR material.For example, propose in patent document the 1st, 2 and improve the DR material of formability Material.
Propose a kind of DR steel in patent document 1, it is characterised in that containing C in terms of quality %：0.02%～ 0.06%th, Si：Less than 0.03%, Mn：0.05%～0.5%, P：Less than 0.02%, S：Less than 0.02%, Al：0.02%～ 0.10%th, N：0.008%～0.015%, the solid solution N amount in the steel plate that surplus is made up of Fe and inevitable impurity (Ntotal-NasAlN) being more than 0.006%, the percentage of total elongation value of the rolling direction after Ageing Treatment is more than 10%, timeliness The percentage of total elongation value of the plate width direction after process is more than 5%, and, the average Lankford value after Ageing Treatment be 1.0 with Under.
Proposing the high-intensity welding tank sheet metal that a kind of flange has excellent moldability in patent document 2, its feature exists In in terms of quality %, containing C：More than 0.04% and less than 0.08%, Si：Less than 0.02%, Mn：Less than 1.0%, P： Less than 0.04%, S：Less than 0.05%, Al：Less than 0.1%, N：Less than 0.005～0.02%, the solid solution C being solid-solution in steel plate Meet the relation of 50ppm≤solid solution C+ solid solution N≤200ppm with the total amount of solid solution N, the solid solution C in steel plate is below 50ppm, steel Solid solution N in plate is more than 50ppm, and surplus is made up of Fe and inevitable impurity.
Prior art literature
Patent document
Patent document 1：International Publication No. 2008/018531
Patent document 2：Japanese Unexamined Patent Publication 2002-294399 publication
Content of the invention
Invent problem to be solved
But, above-mentioned prior art exists problem as follows.
In the technology described in patent document 1, the condition such as the hop count of rivet according to EOE tank processing not necessarily can obtain To good formability.In addition, in the technology described in patent document 1, the processability such as flange processability of built-up tin is not Fully.
In the technology described in patent document 2, insufficient for the rivet formability manufacturing needed for EOE tank.In addition, be Reduction solid solution C measures and needs long Wetted constructures, manufactures efficiency and reduces.
The present invention completes in view of the foregoing, its object is to solve above-mentioned problem of the prior art and provides one Plant high-strength steel sheet and the manufacture method thereof with good formability (processability) and intensity.
For solving the method for problem
The present inventors conducts in-depth research to solve the problems referred to above.It was found that by optimizing composition of steel, hot rolling Condition, cold rolling condition, annealing conditions and secondary cold-rolling condition (DR condition), can make drawing of the rolling right angle orientation after Ageing Treatment Stretching intensity is more than 530MPa, and percentage elongation is more than 7%.Furthermore, it was found that the dislocation of ferrite average grain diameter, thickness of slab 1/4 is close Degree contributes to taking into account above-mentioned tensile strength and above-mentioned percentage elongation, thus completes the present invention.Specifically, the following institute of the present invention State.
(1) a kind of high-strength steel sheet, it is characterised in that have in terms of quality % containing C：More than 0.010% and 0.080% Below, Si：Less than 0.05%, Mn：More than 0.10% and less than 0.70%, P：Less than 0.03%, S：Less than 0.020%, Al： More than 0.005% and less than 0.070%, N：More than 0.0120% and less than 0.0180%, surplus is by Fe and inevitably miscellaneous The one-tenth that matter is constituted is grouped into, and in contained above-mentioned N, the N content as solid solution N is more than 0.0100%, ferrite average particle Footpath is less than 7.0 μm, and from surface, the dislocation density of 1/4 depth location of thickness of slab is 4.0 × 1014m-2Above and 2.0 × 1015m-2Hereinafter, the tensile strength of the rolling right angle orientation after Ageing Treatment is more than 530MPa, and percentage elongation is more than 7%.
(2) manufacture method of a kind of high-strength steel sheet described in (1), it is characterised in that have：Hot-rolled process, by steel billet Heating-up temperature more than 1180 DEG C heats, and hot rolling finishing temperature being set as, 820～900 DEG C roll, at 640 DEG C Following coiling temperature batches；Once cold rolling operation, after above-mentioned hot-rolled process, carries out pickling, with the rolling of more than 85% Rate carries out cold rolling；Annealing operation, after above-mentioned once cold rolling operation, more than 620 DEG C and less than 690 DEG C anneal；And secondary Cold rolling process, after above-mentioned annealing operation, carries out the secondary cold-rolling that rolling rate is 8～20%.
Invention effect
The high-strength steel sheet of the present invention is grouped into by specific one-tenth and constitutes, and ferrite average grain diameter is less than 7.0 μm, from table The dislocation density of 1/4 depth location that thickness of slab is played in face is 4.0 × 1014m-2Above and 2.0 × 1015m-2Hereinafter, thus, at timeliness The tensile strength of the rolling right angle orientation after reason is more than 530MPa, and percentage elongation is more than 7%.
As described above, the high-strength steel sheet of the present invention has high formability, thus, it is also possible to be suitably applied enforcement rivet In the purposes that processing, flange processing form.Particularly, the tensile strength of the high-strength steel sheet of the present invention be 530MPa with On, there is sufficient intensity, therefore, compared with conventional steel plate, even if suppression thickness of slab also can form tank body, the tank of high-quality Lid.It by making thickness of slab thinning, is capable of resources conservation, cost degradation.
In addition, the high-strength steel sheet of the present invention excellent in terms of formability and intensity can not only be expected to be applied to various Metal can, but also can expect to be applied to the extensive model such as tinning, various household electrical appliances electric component, automotive part in dry cell Enclose.
Detailed description of the invention
Hereinafter, embodiments of the present invention are illustrated.It should be noted that the present invention is not limited to following enforcement Mode.
The high-strength steel sheet of the present invention has specific one-tenth and is grouped into, and is adjusted to ferrite average grain diameter, thickness of slab The dislocation density of 1/4 position is in specific scope.As a result, the high-strength steel sheet of the present invention is high intensity and formability Excellent.Hereinafter, to becoming to be grouped into, the material of ferrite average grain diameter, the dislocation density of thickness of slab 1/4 position, high-strength steel sheet (high Intensity, high formability), the manufacture method of high-strength steel sheet illustrates successively.
<One-tenth is grouped into>
The high-strength steel sheet of the present invention has following one-tenth and is grouped into：In terms of quality %, containing C：More than 0.010% and Less than 0.080%, Si：Less than 0.05%, Mn：More than 0.10% and less than 0.70%, P：Less than 0.03%, S：0.020% with Under, Al：More than 0.005% and less than 0.070%, N：More than 0.0120% and less than 0.0180%, surplus is by Fe and can not keep away The impurity exempted from is constituted.Further, in contained above-mentioned N, the N content as solid solution N is more than 0.0100%.Hereinafter, to each one-tenth Divide and illustrate.In the following description, " % " refers to " quality % ".
C：More than 0.010% and less than 0.080%
C contributes to improve the element of the intensity of steel plate.By C content is set as more than 0.010%, timeliness can be made The tensile strength of the rolling right angle orientation after process is more than 530MPa.When C content is more than 0.080%, rolling after Ageing Treatment The percentage elongation of right angle orientation processed decreases below 7%, and flange processability, the rivet formability of steel plate reduce.Accordingly, it would be desirable to by C Content is set as less than 0.080%.From the viewpoint of guaranteeing good flange processability, rivet formability, preferably by C content It is set smaller than 0.040%.C content is more many more can make ferrite average grain diameter miniaturization, therefore, in order to make steel plate high-strength C content is preferably set as more than 0.020% by degree.
Si：Less than 0.05%
When steel plate contains a large amount of Si, because surface enrichment makes the surface rationality deterioration of steel plate, the corrosion resistance of steel plate reduces. Therefore, Si content needs to be set as less than 0.05%.It is preferably less than 0.03%.
Mn：More than 0.10% and less than 0.70%
Mn has the effect making the hardness of steel plate improve by solution strengthening.In addition, Mn is had prevent by forming MnS The effect that the high-temperature ductility that S contained in invar causes reduces.In order to obtain the effect above, need to be set as Mn content More than 0.10%.Additionally, Mn has the effect making particle diameter miniaturization, it is therefore preferable that Mn content is set as more than 0.20%.This Outward, by reduce N diffusion velocity, have suppression AlN generation and it is easy to ensure that the effect of solid solution N, particularly make stretching Intensity high intensity is to being effective during more than 590MPa.Therefore, further preferably Mn content is set greater than 0.50%.Separately Outward, when adding excessive Mn, not only the effect above is saturated, and percentage elongation significantly reduces, therefore, Mn content be set as 0.70% with Under.
P：Less than 0.03%
During containing a large amount of P, because of excessive hardening, central authorities segregation and formability is reduced.During in addition, contain a large amount of P, Corrosion resistance reduces.Therefore, P content is set as less than 0.03%.It is preferably less than 0.02%.
S：Less than 0.020%
S forms sulfide in steel and makes the high-temperature ductility of steel plate reduce.Therefore, S content is set as less than 0.020%. It is preferably less than 0.015%.
Al：More than 0.005% and less than 0.070%
Al is the element adding as deoxidier.In order to obtain the effect above, need Al content is set as 0.005% Above.The solid solution N in steel is made to reduce owing to Al and N forms AlN.When solid solution N reduces, the intensity of steel plate reduces, and therefore, Al contains Amount is set as less than 0.070%.From the viewpoint of the solid solution N stably guaranteeing more than 0.0100% measures, preferably by Al content It is set as less than 0.020%, be more preferably set as less than 0.018%.
N：More than 0.0120% and less than 0.0180%, solid solution N：More than 0.0100%
N exists by way of with solid solution N and contributes to the high intensity of steel plate.Additionally, by having more than 0.010% Solid solution N, the importing of dislocation during secondary cold-rolling is promoted, the balance of high intensityization and formability improves.For the effect above, Need the N content as solid solution N is set as more than 0.0100%.More preferably more than 0.0120%.Further, in order to make Solid solution N is more than 0.0100%, needs N content is set as more than 0.0120%.Preferably N content for more than 0.0130%.In order to make solid solution N be stably more than 0.0120%, one of preferred compositions is following, and above condition suppresses The generation of the AlN in manufacturing process, described condition is：(1) containing the Mn more than 0.50%；(2) by the coiling temperature in hot rolling It is set as less than 640 DEG C, be preferably set to less than 600 DEG C, be further preferably set as less than 580 DEG C；(3) annealing temperature is set It is set to less than 690 DEG C, be further preferably set at less than 680 DEG C.In order to as forming higher tank intensity or further The situation of thin-walled property and make tensile strength high intensity to forming the height that percentage elongation is more than 10% in the case of more than 600MPa Formability, whole three conditions of preferred compositions.On the other hand, when containing a large amount of N, percentage elongation reduces, and rivet formability, flange add Work all reduces.Therefore, N content is set as less than 0.0180%.It is preferably less than 0.0170%.N content is made to be above-mentioned scope When, the N content as solid solution N is less than 0.0180%.
Balance of iron beyond above-mentioned neccessary composition and inevitable impurity.
<Ferrite average grain diameter：Less than 7.0 μm>
The dislocation density meeting mentioned component composition and thickness of slab 1/4 depth location is in the steel plate of specific scope For, by being less than 7.0 μm by ferrite crystal grain miniaturization to ferrite average grain diameter, thus, high intensity and formability Balance improve.Additionally, by by ferrite average grain diameter miniaturization, also there is the shaggy advantage after suppression processing. Therefore, ferrite average grain diameter is preferably less than 6.5 μm.It should be noted that ferrite average grain diameter uses passes through embodiment The value that described method measures.Ferrite particle diameter after annealing is more fine, and the importing of the dislocation in secondary cold-rolling is more promoted Entering, even if also can obtain high intensity with lower rolling rate, therefore, high intensityization improves further with the balance of formability. In view of the ferrite after secondary cold-rolling when (before secondary cold-rolling) after comparing annealing and the ferrite average grain diameter after secondary cold-rolling Average grain diameter can reduce, in order to obtain the effect above, ferrite average grain diameter after secondary cold-rolling more preferably 6.0 μm with Under.The lower limit of ferrite average grain diameter is not particularly limited, and when becoming over fine, high intensityization drops with the balance of formability Low, for the above reasons, preferably more than 1.0 μm.It should be noted that the structure of steel of the present invention is based on ferrite, iron Ferritic phase is more than 98 volume %.
<The dislocation density of thickness of slab 1/4 position：4.0×1014m-2Above and 2.0 × 1015m-2Below>
In the present invention, in order to take into account intensity and the formability of steel plate, the control of the dislocation density in steel plate is critically important.? In the present invention, for high intensity, the dislocation density by thickness of slab 1/4 depth location is needed to be set as 4.0 × 1014m-2Above.Cross The dislocation density of amount can induce the generation of hole when shaping, and makes the formability of steel plate reduce.Accordingly, it would be desirable to by close for above-mentioned dislocation Degree is set as 2.0 × 1015m-2Below.In order to make dislocation density be above-mentioned scope, particularly make solid solution N amount be 0.0100% with Upper, be preferably more than 0.0120%, make ferrite average grain diameter be less than 7.0 μm, preferably less than 6.5 μm, further preferably Be less than 6.0 μm critically important.It should be noted that the dislocation density of thickness of slab 1/4 position uses by the side described in embodiment The value that method measures.
<Material>
The high-strength steel sheet of the present invention has mentioned component composition, and ferrite average grain diameter is adjusted to less than 7.0 μm, plate The dislocation density of thick 1/4 position is adjusted to 4.0 × 1014m-2Above and 2.0 × 1015m-2Hereinafter, therefore, it is the same of high intensity When there is high formability.
Generally, in the case that the thickness of steel plate is thin, it is very difficult to take into account high intensity and high formability." thickness is thin " refers to For below 0.26mm.In the case of the present invention, the thick steel plate for 0.12mm of connecting plate can take into account high intensity and high formability.
The tensile strength of rolling right angle orientation after high intensity refers to Ageing Treatment is more than 530MPa.If above-mentioned stretching Intensity is more than 530MPa, then when being configured to cover, tank body, it can be ensured that sufficient tank intensity.Above-mentioned tensile strength is excellent Elect more than 550MPa as, more preferably more than 590MPa.When above-mentioned tensile strength is more than 550MPa, though special at thickness Also high intensity and high formability can be taken into account in the case of not thin." thickness is extremely thin " refers to as below 0.18mm.
The percentage elongation of rolling right angle orientation after high formability refers to Ageing Treatment is more than 7%.If above-mentioned percentage elongation It is more than 7%, then, when the high-strength steel sheet of the present invention is applied to tank body, EOE tank, the manufacture of tank body can be guaranteed fully Required flange processability, EOE tank manufacture required rivet formability.Tensile strength is the high intensity of more than 550MPa In the case of, further requirement formability, therefore, the percentage elongation of the rolling right angle orientation after Ageing Treatment be preferably 10% with On.
It should be noted that when shaping tank, steel plate is formed after in most cases sintering application on steel plate, because of This, need to be equivalent to sinter application Ageing Treatment after material evaluate.
<The manufacture method of high-strength steel sheet>
Hereinafter, a case of the manufacture method of the high-strength steel sheet of the present invention is illustrated.
The high-strength steel sheet of the present invention can be cold by having hot-rolled process, once cold rolling operation, annealing operation and secondary The method rolling operation manufactures.Hereinafter, each operation is illustrated.
Hot-rolled process
Hot-rolled process refers to following operation：By have beyond solid solution N mentioned component composition steel billet (solid solution N can meet Also can be unsatisfactory for) heating-up temperature more than 1180 DEG C heats, and hot rolling finishing temperature being set as, 820～900 DEG C are entered Row rolling, the coiling temperature below 640 DEG C batches.
When billet heating temperature is too low, a part of AlN is unfused, and solid solution N measures reduction.Therefore, heating-up temperature is set It is more than 1180 DEG C.It is preferably more than 1200 DEG C.The upper limit of heating-up temperature does not has special provision, but when heating-up temperature is too high, has When can produce excessive oxide skin and produce defect at product surface.Therefore, heating-up temperature is preferably set to less than 1300 DEG C.
When hot rolling finishing temperature is higher than 900 DEG C, the particle diameter in hot rolled plate becomes thick, and thus, the particle diameter in annealed sheet becomes Obtaining thick, the hardness of steel plate reduces.Therefore, hot rolling finishing temperature is set as less than 900 DEG C.Hot rolling finishing temperature is less than 820 DEG C When, become the rolling of below Ar3 transformation temperature, because generating coarse grain, residual process tissue makes formability reduce.Therefore, heat Roll finishing temperature and be set as more than 820 DEG C.It is preferably more than 840 DEG C.
When coiling temperature is more than 640 DEG C, batch the middle a large amount of AlN of generation and solid solution N amount reduces.In addition, coiling temperature exceedes When 640 DEG C, the particle diameter of hot rolled plate becomes thick, the particle diameter also coarsening after thus annealing.Therefore, coiling temperature is set as 640 Below DEG C.It is preferably less than 600 DEG C, more preferably less than 580 DEG C.The lower limit of coiling temperature is not particularly limited, and batches When temperature is too low, the temperature change in sometimes cooling down increases, and tensile strength, the variation of percentage elongation increase.It is therefore preferable that will batch Temperature is set as more than 500 DEG C.
Once cold rolling operation
Once cold rolling operation refers to following operation：After hot-rolled process, carrying out pickling, the rolling rate with more than 85% carries out one Secondary cold rolling.
As long as acid washing conditions can remove superficial oxidation skin, condition does not has special provision.Conventional method can be passed through Carry out pickling.
By suitably regulating the rolling rate of once cold rolling, the particle diameter miniaturization after annealing can be made, improve tensile strength Balance with percentage elongation.In order to obtain the effect above, rolling rate is set as more than 85%.But, when rolling rate becomes excessive, Tensile strength, the intra-face anisotropy of percentage elongation increase, and formability reduces.Therefore, the rolling rate in this operation is preferably set to Less than 91.5%.
Annealing operation
Annealing operation refers to following operation：After cold rolling process, more than 620 DEG C and the annealing temperature of less than 690 DEG C is carried out Annealing.
In order to ensure formability, need abundant recrystallization in annealing.Therefore, annealing temperature need to be set as 620 DEG C with On.When annealing temperature is too high, ferrite average grain diameter coarsening, tensile strength reduces with the balance of percentage elongation.Therefore, annealing temperature Degree is set as less than 690 DEG C.When annealing temperature raises, generating AlN, solid solution N amount is easily reduced, it is therefore preferable that by annealing temperature It is set as less than 680 DEG C.Method for annealing is not particularly limited, from the viewpoint of the uniformity of material, and preferably continuous annealing method. It should be noted that the retention time in annealing operation is not particularly limited, from the viewpoint of the uniformity of steel billet temperature, excellent Elect as more than 5 seconds, from the viewpoint of the coarsening preventing ferrite average grain diameter, preferably less than 90 seconds.
Secondary cold-rolling (DR rolling) operation
Secondary cold-rolling operation refers to following operation：After annealing operation, carry out the secondary cold-rolling that rolling rate is 8～20%.
Steel plate after annealing is rolled and high intensity by secondary.In addition, the thickness of steel plate is rolled thinning by secondary.For The dislocation density making from surface thickness of slab 1/4 depth location raises and obtains the steel plate of high intensity, by rolling during secondary cold-rolling Rate processed (DR leads) is set as more than 8%.When DR leads too high, dislocation density excessively raises, and formability deteriorates.Therefore, DR is led set It is set to less than 20%.In the case of especially requiring formability, preferably DR is led and be set as less than 15%.
By the above-mentioned high-strength steel sheet that can obtain the present invention.Even if plating, chemistry are carried out to the steel plate obtaining at this The surface treatments such as conversion processing also will not lose invention effect.
Embodiment
Melting has that the one-tenth of the steel symbol A～N shown in table 1 is grouped into, surplus is made up of Fe and inevitable impurity Steel, obtains steel billet.After obtained steel billet is heated under the conditions shown in Table 2, carry out hot rolling, remove oxidation by pickling Skin, then carries out once cold rolling with the once cold rolling rate shown in table 2, anneals in each annealing temperature in continuous annealing furnace, Carry out secondary cold-rolling (DR rolling) with each secondary cold-rolling rate, obtain steel plate (the steel plate symbol No.1 that thickness of slab is 0.15～0.26mm ～22).Two-sided enforcement one side 2.8g/m to obtained steel plate2Tin plating, this tin plate is carried out by following method Evaluating characteristics.
Solid solution N measures
Solid solution N amount is by deducting to be come by the N as AlN amount utilizing the extractive analysis of 10%Br methyl alcohol to measure from total N content Evaluate.
The tensile strength of the rolling right angle orientation after Ageing Treatment, percentage elongation
After 210 DEG C of Ageing Treatment being equivalent to sinter application carrying out 10 minutes, cut JIS5 from rolling right angle orientation Number tension test piece, according to JIS Z 2241, evaluates to tensile strength and percentage elongation (percentage of total elongation).
Ferrite average grain diameter
Embedded rolling direction cross section, after grinding, utilize nital to carry out corroding and after making crystal boundary manifest, according to JIS G 0551, measures average crystallite particle diameter by patterning method, evaluates ferrite average grain diameter.
Dislocation density
Dislocation density is measured by Williamson-Hall method (Williamson's Hall process).That is, deep at thickness of slab 1/4 The half-peak breadth of the diffraction maximum in degree position finding (110) (211) (220) face, uses the half-peak breadth of unstrained Si sample to be corrected After, obtain strain stress, by ρ=14.4 ε2/(0.25×10-9)2Evaluate dislocation density (m-2).
EOE rivet formability
After 210 DEG C of Ageing Treatment being equivalent to sinter application carrying out 10 minutes, shape EOE handle installation riveting Nail, evaluates to rivet formability.Rivet is shaped and is carried out by the press process of three phases, carries out tube reducing after the convex shaping of drum (drawing) processes the straight neck rivet that shape goes out a diameter of 4.0mm, height is 2.5mm.Fold will be produced on rivet surface, split The situation of line be evaluated as "×", by not producing fold, the situation of crackle is evaluated as "○".
Tank body flangeability
After 210 DEG C of Ageing Treatment being equivalent to sinter application carrying out 10 minutes, carrying out external diameter by seam weld is The tank body of 52.8mm shapes, and it is carry out flange to be machined to external diameter be 55.4mm after 50.4mm that end necking down is machined to external diameter, right Have or not flange crack generation to evaluate.Tank body shapes makes 190g beverage can size, welds along steel plate rolling direction. Necking down processing is carried out by mould necking down (ダ Ren ネ Star Network) mode, and flange processing is carried out by rotary flange mode.Will be at flange The situation that processing department cracks is evaluated as "×", and situation about not cracking is evaluated as "○".
Tank intensity
Above-mentioned necking down processing, flange are processed the sample obtaining and rolled tightly lid, produces tank body, measure tank by indentation test Body intensity.To as the tank body central with weld part opposition side, pressing front-end radius is 10mm, the pressure head of a length of 42mm, Measure load when tank body portion buckles, be well evaluated as "○" for being considered as tank intensity during more than 70N, will be less than 70N It is evaluated as "×".It should be noted that the sample cracking in processing flange and can not being fabricated to tank body is set to "-".
Show the result in table 3.In example of the present invention, be all tensile strength be more than 530MPa, percentage elongation be more than 7%, Ferrite crystal grain footpath is less than 7.0 μm, the dislocation density of thickness of slab 1/4 depth location is 4.0 × 1014m-2Above and 2.0 × 1015m-2Below, armor plate strength and having excellent moldability.On the other hand, in a comparative example, a certain above poor in above-mentioned characteristic.
Table 1
(quality %)
Steel symbol C Si Mn P S AI N Remarks
A 0.034 0.01 0.24 0.012 0.011 0.015 0.0155 Example of the present invention
B 0.020 0.02 0.30 0.014 0.010 0.012 0.0144 Example of the present invention
C 0.039 0.01 0.14 0.009 0.013 0.010 0.0163 Example of the present invention
D 0.035 0.01 0.58 0.013 0.009 0.018 0.0122 Example of the present invention
E 0.028 0.01 0.70 0.008 0.008 0.008 0.0175 Example of the present invention
F 0.078 0.01 0.35 0.010 0.009 0.019 0.0132 Example of the present invention
G 0.083 0.01 0.26 0.013 0.012 0.015 0.0132 Comparative example
H 0.005 0.01 0.22 0.011 0.010 0.016 0.0149 Comparative example
1 0.036 0.01 0.25 0.009 0.012 0.012 0.0191 Comparative example
J 0.031 0.01 0.35 0.010 0.008 0.090 0.0038 Comparative example
K 0.034 0.01 0.35 0.013 0.010 0.023 0.0149 Example of the present invention
L 0.042 0.01 0.26 0.015 0.011 0.016 0.0126 Example of the present invention
M 0.022 0.01 0.61 0.013 0.009 0.018 0.0153 Example of the present invention
N 0.035 0.01 0.51 0.012 0.010 0.017 0.0148 Example of the present invention
Table 2
Table 3

Claims (2)

1. a high-strength steel sheet, it is characterised in that
Have in terms of quality % containing C：More than 0.010% and less than 0.080%, Si：Less than 0.05%, Mn：More than 0.10% And less than 0.70%, P：Less than 0.03%, S：Less than 0.020%, Al：More than 0.005% and less than 0.070%, N： More than 0.0120% and less than 0.0180%, surplus is become to be grouped into by what Fe was constituted with inevitable impurity,
In contained described N, the N content as solid solution N is more than 0.0100%,
Ferrite average grain diameter is less than 7.0 μm,
From surface, the dislocation density of 1/4 depth location of thickness of slab is 4.0 × 1014m-2Above and 2.0 × 1015m-2Hereinafter,
The tensile strength of the rolling right angle orientation after Ageing Treatment is more than 530MPa, and percentage elongation is more than 7%.
2. the manufacture method of the high-strength steel sheet described in a claim 1, it is characterised in that have：
Heating-up temperature more than 1180 DEG C for the steel billet is heated by hot-rolled process, hot rolling finishing temperature is set as 820～ 900 DEG C roll, and the coiling temperature below 640 DEG C batches；
Once cold rolling operation, after described hot-rolled process, carries out pickling, and the rolling rate with more than 85% carries out cold rolling；
Annealing operation, after described once cold rolling operation, more than 620 DEG C and less than 690 DEG C anneal；With
Secondary cold-rolling operation, after described annealing operation, carries out the secondary cold-rolling that rolling rate is 8～20%.
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