CN104160052A - Steel sheet for hot pressing use, press-molded article, and method for producing press-molded article - Google Patents

Steel sheet for hot pressing use, press-molded article, and method for producing press-molded article Download PDF

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Publication number
CN104160052A
CN104160052A CN201380012504.9A CN201380012504A CN104160052A CN 104160052 A CN104160052 A CN 104160052A CN 201380012504 A CN201380012504 A CN 201380012504A CN 104160052 A CN104160052 A CN 104160052A
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area
steel plate
temperature
martensite
retained austenite
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CN104160052B (en
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村上俊夫
内藤纯也
冲田圭介
池田周之
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Kobe Steel Ltd
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Kobe Steel Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/20—Deep-drawing
    • B21D22/208—Deep-drawing by heating the blank or deep-drawing associated with heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D37/00—Tools as parts of machines covered by this subclass
    • B21D37/16—Heating or cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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    • C21—METALLURGY OF IRON
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    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D2221/00—Treating localised areas of an article
    • 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
    • C21D2221/00—Treating localised areas of an article
    • C21D2221/10—Differential treatment of inner with respect to outer regions, e.g. core and periphery, respectively

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  • Chemical & Material Sciences (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

A steel sheet for hot pressing use according to the present invention has a specified chemical component composition, wherein some of Ti-containing precipitates contained in the steel sheet, each of which has an equivalent circle diameter of 30 nm or less, have an average equivalent circle diameter of 3 nm or more, the amount of precipitated Ti and the total amount of Ti in the steel fulfill the relationship represented by formula (1) shown below, and the sum total of the fraction of bainite and the fraction of martensite in the metallographic structure is 80% by area or more. Amount of precipitated Ti (mass%) - 3.4[N] > 0.5[(total amount of Ti (mass%)) - 3.4[N]] ...(1) (In formula (1), [N] represents the content (mass%) of N in the steel.)

Description

The manufacture method of steel plate and stamping product and stamping product for hot pressing
Technical field
While the present invention relates to manufacture the structural parts of automobile, use, be applicable to the hot pressing steel plate of hot compacting, with the stamping product that obtained with steel plate by such hot pressing, and the manufacture method of stamping product, particularly relate to when pre-heated steel plate (base substrate) shaping is processed into set shape, in giving shape, implement thermal treatment and obtain the intensity of regulation hot compacting method be suitable for useful hot pressing steel plate, and stamping product and for the manufacture of the useful method of so stamping product.
Background technology
One of countermeasure improving as the fuel efficiency of the automobile being caused by global environment problem, the lightweight of car body advances, the steel plate high strength as far as possible that need to make automobile use.On the other hand, if make steel plate high strength, the shape when stamping reduces precision.
Set out thus, hot compacting method is used in part manufacture, its temperature by steel plate being heated to regulation (for example, form the temperature of austenite phase) and reduce after intensity, for example, form than the mould of steel plate low (room temperature) by temperature, thereby in giving shape, utilize the chilling thermal treatment (quenching) of both temperature difference, to guarantee the intensity after shaping.Further, so hot press-formed method, except pressure sintering, also with the various title addresses such as method for hot forming, hot stamped process, hot padding method, die quenching method.
Fig. 1 is the diagrammatic illustration figure that represents that the mould for implementing above-mentioned such hot compacting forms, in figure, 1 represents drift, 2 represent punch die, 3 represent blank holder, 4 represent steel plate (base substrate), and BHF represents pressure-pad-force, and rp represents drift shoulder radius, rd represents punch die shoulder radius, and CL represents the gap between drift/punch die.In addition, among these parts, drift 1 and punch die 2 its constituted modes are, are formed with path 1a, the 2a that can make heat-eliminating medium (for example water) pass through in inside separately, make by heat-eliminating medium, these members to be obtained in this path cooling.
For example, while using such mould to carry out hot compacting (, hot deep-draw processing), steel plate (base substrate) 4 is heated to (A c1transformation temperature～A c3transformation temperature) two phase region temperature or A c3single-phase territory temperature more than transformation temperature, starts to be shaped to make it softening state.That is, the steel plate in the condition of high temperature 4 is clipped in to the state between punch die 2 and blank holder 3, steel plate 4 is pressed in the hole of punch die 2 with drift 1, dwindles the external diameter of steel plate 4 while be configured as the corresponding shape of profile of drift 1.In addition, in being shaped, carry out cooling to drift 1 and punch die 2, thereby carry out from steel plate 4 to mould the heat extraction of (drift 1 and punch die 2), and further keep cooling and implement the quenching of former material at shaping bottom dead centre (drift front end is positioned at the innermost moment: the state shown in Fig. 1).By implementing such moulding method, can obtain the molding of the good 1500MPa level of dimensional precision, and with cold conditions under the be shaped situation comparison of part of equality strength rank, can reduce shaping load, therefore the charge capacity of pressing machine is very little.
As present widely used hot pressing steel plate, the known hot pressing steel plate having using 22MnB5 steel as former material.This steel plate tensile strength is 1500MPa, and unit elongation is 6～8% left and right, is applicable to shock-resistant member (do one's utmost not make it distortion when collision, the member of fracture does not occur).But, because unit elongation (ductility) is low, so be difficult to be applicable to the part that need to be out of shape as energy-absorbing member.
As the hot pressing steel plate of bringing into play good unit elongation, for example, also propose to have the such technology of patent documentation 1～4.In these technology, be by the carbon content in steel plate is set in to various scopes, adjust the basic intensity rank of each steel plate, and by importing the high ferrite of deformability, dwindle ferrite and martensitic median size, thereby realize the raising of unit elongation.These technology, although effective to the raising of unit elongation,, from the viewpoint improving with the corresponding unit elongation of the intensity of steel plate, still also insufficient.For example, tensile strength TS is steel plate more than 1470MPa, and unit elongation EL is 10.2% left and right to the maximum, requires further to improve.
On the other hand, compared with the hot padding molding studied up to now, in the lower molding of intensity rank, for example tensile strength TS is 980MPa level and 1180MPa level, while colding pressing, on forming accuracy, also have problems, improve countermeasure as it, just have the demand for low strength hot pressing.At this moment, need to significantly improve the EAC of molding.
Particularly in recent years, in 1 part, the exploitation of the poor technology of distribution intensity advances.As such technology, following technology is proposed, the position that should prevent distortion is high strength (high strength side: shock-resistant position side), and the place that needs energy absorption is low strength and is high ductibility (low strength side: energy absorption position side).For example; in medium-sized or above car; in the time of side collision and when rearward collision, consider the property taken into account (also will protect the function of the other side's side when compact car collision); have in the part of B post and floor side member, make it to have the situation of shock-resistance and these two kinds of functional parts of energy absorption.In order to make such part, propose just like inferior method: (a) in common hot pressing with on steel plate, even engage heating, die quenching to uniform temp is still low intensive steel plate (tailor welded: TWB) method; (b) give difference to the speed of cooling in mould and the method for each region of steel plate being given to intensity difference; (c) give difference for the Heating temperature in each region of steel plate and the method for giving intensity difference.
In these technology, in high strength side (shock-resistant position side), tensile strength can reach 1500MPa level, but in low strength side (energy absorption position side), the maximum tensile strength is 700MPa, unit elongation EL is 17% left and right, in order further to improve EAC, requires more under high strength, realizing high ductibility.
[prior art document]
[patent documentation]
Patent documentation 1: TOHKEMY 2010-65292 communique
Patent documentation 2: TOHKEMY 2010-65293 communique
Patent documentation 3: TOHKEMY 2010-65294 communique
Patent documentation 4: TOHKEMY 2010-65295 communique
Summary of the invention
The present invention In view of the foregoing forms, its object is, a kind of hot pressing steel plate is provided, and provide the stamping product of having given play to above-mentioned such characteristic, useful method with the stamping product for the manufacture of such, when hot pressing used requires uniform characteristic with steel plate in molding, it is useful on the hot compacting product that can obtain the balance that can reach with high level high strength and unit elongation; In single molding, require while having the region that is equivalent to shock-resistant position and energy absorption position, it is useful on the stamping product of balance that obtain corresponding regional and can reach with high level high strength and unit elongation.
The what is called hot pressing steel plate of the present invention that can reach above-mentioned purpose, is characterized in that, described steel plate contains respectively
C:0.15～0.5% (the meaning of quality %.Below, relate to chemical composition composition all with.)、
Si：0.2～3％、
Mn：0.5～3％、
P:0.05% following (not containing 0%),
S:0.05% following (not containing 0%),
Al：0.01～1％、
B：0.0002～0.01％、
Ti:3.4[N]+more than 0.01% and 3.4[N]+[wherein, [N] represents the content (quality %) of N] below 0.1% and
N:0.0010～0.01%, surplus is made up of iron and inevitable impurity,
Contained containing among Ti precipitate in steel plate, diameter of equivalent circle is that the average equivalent circular diameter containing Ti precipitate below 30nm is more than 3nm, and the Ti amount of separating out in steel and total Ti content meet the relation of following (1) formula, and in metal structure, the total of bainite and martensite divides rate more than 80 area %.Further, so-called " diameter of equivalent circle ", is for example, while being conceived to contain the size (area) of Ti precipitate (TiC), is converted into the diameter (" average equivalent circular diameter " is its mean value) of bowlder of the same area.
Separate out Ti amount (quality %)-3.4[N] > 0.5 × [total Ti content (quality %)-3.4[N]] ... (1)
(in (1) formula, [N] represents the content (quality %) of the N in steel)
, as required, as other element, also contain as inferior also useful with in steel plate at hot compacting of the present invention: more than one that (a) select from the group that V, Nb and Zr formed: add up to (not containing 0%) below 0.1%; (b) more than one that select the group who forms from Cu, Ni, Cr and Mo: add up to (not containing 0%) below 1%; (c) more than one that select the group who forms from Mg, Ca and REM: add up to 0.01% below and (do not contain 0%), according to the kind of contained element, the characteristic of stamping product is further improved.
The manufacture method that can reach the what is called stamping product of the present invention of above-mentioned purpose, is characterized in that, by above-mentioned such hot pressing steel plate of the present invention, is heated to A c1transformation temperature+20 DEG C above and A c3after the following temperature in transformation temperature-20 DEG C, start stampingly, after the neutralization that is shaped is shaped and finishes, guarantee more than 20 DEG C/sec average cooling rates on one side in mould, one side is cooled to than bainitic transformation and starts below the temperature of low 100 DEG C of temperature Bs.
In the stamping product that obtained by this manufacture method, in metal structure, retained austenite: 3～20 area %, annealing martensite and/or annealing bainite: 30～87 area %, as-quenched condition martensite: 10～67 area %, and the carbon amount in described retained austenite is more than 0.60%, in molding, can also reach using high level the balance of high strength and unit elongation as uniform characteristic.Further, the area occupation ratio of annealing martensite and/or annealing bainite, in the time containing two sides and organize, the meaning is the total area occupation ratio of two kinds of tissues; During by the organizational composition of one party, the meaning is the area occupation ratio of this tissue.
On the other hand, can reach other manufacture method of the what is called stamping product of the present invention of above-mentioned purpose, it is characterized in that, use above-mentioned such hot pressing steel plate of the present invention, the heating region of steel plate is divided into 2 regions, a region is heated to A c3temperature more than transformation temperature and below 950 DEG C, and another region is heated to A c1transformation temperature+20 DEG C above and A c3after the following temperature in transformation temperature-20 DEG C, start stampingly, after the neutralization that is shaped is shaped and finishes, guarantee more than 20 DEG C/sec average cooling rates on one side in mould, one side is cooled to martensitic transformation and starts the temperature below temperature Ms.
In the stamping product that obtained by this manufacture method, there is first area and second area, described first area is: in metal structure, retained austenite: 3～20 area %, martensite: more than 80 area %; Described second area is: in metal structure, retained austenite: 3～20 area %, annealing martensite and/or annealing bainite: 30～87 area %, as-quenched condition martensite: 10～67 area %, and the carbon amount in described retained austenite is more than 0.60%, in so stamping product, corresponding regional, can reach with high level the balance of high strength and unit elongation, in single molding, have the region that is equivalent to shock-resistant position and energy absorption position.
According to the present invention, because the steel plate using has specified chemical composition composition closely, and control the size containing Ti precipitate, control its eduction rate for the Ti that does not form TiN in addition, in addition adjusted the ratio of tempering hard phase (martensitic phase, bainite equate) and hard phase (as-quenched condition martensitic phase) and retained austenite phase for metal structure, so condition is according to the rules carried out hot pressing to it, can make intensity-unit elongation balance of stamping product reach high level.If carry out hot pressing in multiple regions with different conditions in addition, can in single molding, form shock-resistant position and energy absorption position, can reach at each position the balance of high strength and unit elongation with high level.
Brief description of the drawings
Fig. 1 is the diagrammatic illustration figure that represents that the mould for implementing hot compacting forms.
Embodiment
The present inventors are being heated to steel plate after the temperature of regulation, when carrying out hot compacting and manufacturing stamping product, both guaranteed high strength in order to realize can realizing after stamping, demonstrate again the hot pressing steel plate of the so stamping product of good ductility (unit elongation), study from various angles.
It found that, if specify closely the chemical composition composition of hot pressing steel plate, and realize containing the size of Ti precipitate and the control of separating out Ti amount, and make metal structure suitable, carry out hot compacting with prescribed condition for this steel plate, can obtain guaranteeing the retained austenite of specified amount after shaping, improve the stamping product of inherent ductility (residual ductility), thereby completed the present invention.
Use in steel plate in the hot pressing that the present invention is used, need to specify closely chemical composition composition, described in the circumscription of each chemical composition be the reasons are as follows.
[C：0.15～0.5％]
When C requires uniform characteristic in molding for reach the balance of high strength and unit elongation with high level, or while requiring to have the region suitable with energy absorption position with shock-resistant position, particularly guarantee on retained austenite it is important element at low strength, high ductibility position in single molding.When heating in hot compacting, C is multiviscosisty in austenite in addition, can after quenching, make retained austenite form.In addition, the increase that it also contributes to martensite volume, rises intensity.In order to bring into play these effects, it is more than 0.15% needing C content.
But, exceed 0.5% if C content is superfluous, two phase region heating region stenosis are narrow, cannot high level reach in molding high strength while requiring to have uniform characteristic and the balance of unit elongation, or in single molding, require while having the region suitable with energy absorption position with shock-resistant position, be particularly difficult to adjust to the metal structure (with specified amount guarantee the to anneal tissue of martensite and/or annealing bainite) of expection at low strength, high ductibility position.Under C content preferred, be limited to more than 0.17% (more preferably more than 0.20%), be limited to (more preferably below 0.40%) below 0.45% on preferred.
[Si：0.2～3％]
Si is formed cementite at the cooling middle inhibition martensite of die quenching by tempering, or the austenite decomposition of phase transformation not, is bringing into play the effect that retained austenite is formed.In order to bring into play such effect, it is more than 0.2% needing Si content.If Si content is superfluous and exceed 3% in addition, easily form ferrite, in the time of heating, be difficult to single-phaseization, in necessity point rate that can not guarantee bainite and martensite in steel plate for hot pressing.Under Si content preferred, be limited to more than 0.5% (more preferably more than 1.0%), be limited to (more preferably below 2.0%) below 2.5% on preferably.
[Mn：0.5～3％]
Mn improves hardenability, is effective element for the formation of the tissue (ferrite, perlite, bainite etc.) beyond the martensite, the retained austenite that suppress in die quenching cooling.In addition, be the element that makes stabilization of austenite, be the element that contributes to the increase of retained austenite amount.In order to bring into play such effect, need to make Mn contain more than 0.5%.When consideration characteristics, the preferably many situations of Mn content, but the angle that the cost adding from alloy rises is below 3%.Under Mn content preferred, be limited to more than 0.7% (more preferably more than 1.0%), be limited to (more preferably below 2.0%) below 2.5% on preferably.
[P:0.05% following (not containing 0%)]
P is the element inevitably being contained in steel, but because make ductility deteriorated, so preferably do one's utmost to reduce P.But extreme minimizing can cause the increase of steel-making cost, reach 0% and have any problem on manufacturing, be therefore (not containing 0%) below 0.05%.The preferred upper limit of P content is (more preferably below 0.040%) below 0.045%.
[S:0.05% following (not containing 0%)]
S is same with P, is the element unavoidably being contained in steel, because make ductility deteriorated, so preferably do one's utmost to reduce S.But extreme minimizing can cause the increase of steel-making cost, reach 0% and have any problem on manufacturing, be therefore (not containing 0%) below 0.05%.The preferred upper limit of S content is (more preferably below 0.040%) below 0.045%.
[Al：0.01～1％]
Al is useful as deoxidant element, and the solid solution N being present in steel is fixed as AlN, useful for the raising of ductility.In order effectively to bring into play such effect, it is more than 0.01% needing Al content.But, exceed 1%, Al if Al content is superfluous 2o 3generate superfluously, make ductility deteriorated.Further, the preferred lower limit of Al content is more than 0.02% (more preferably more than 0.03%), and the preferred upper limit is (more preferably below 0.6%) below 0.8%.
[B：0.0002～0.01％]
B has the effect at high strength position lateral inhibition ferrite transformation, pearlitic transformation and bainitic transformation, is therefore being heated to (A c1transformation temperature～A c3transformation temperature) two phase region temperature after cooling in, be the formation that prevents ferrite, perlite, bainite, contribute to guarantee the element of retained austenite.For bringing into play such effect, need to make B contain more than 0.0002%, even but exceed 0.01% and contain, effect is also saturated. superfluouslyUnder B content preferred, be limited to more than 0.0003% (more preferably more than 0.0005%), be limited to (more preferably below 0.005%) below 0.008% on preferably.
Above and the 3.4[N of [Ti:3.4[N]+0.01%]+below 0.1%: [N] is the content (quality %) of N]
Ti fix N, maintains B with solid solution condition, thereby the effect of improving of hardenability is manifested.In order to bring into play such effect, importantly make it to contain more more than 0.01% than the stoichiometric ratio of Ti and N [content of N 3.4 times].But, if Ti content become superfluous and than 3.4[N]+more than 0.1%, there is fine dispersion containing Ti precipitate in what formed, hinder the martensitic growth in cooling after two phase regions heating, form the little lath (lath martensite) of long-width ratio, carbon (C) is slack-off to the discharge of the retained austenite between lath, and the carbon amount in retained austenite reduces.Under Ti content preferred, be limited to 3.4[N]+more than 0.02% (more preferably 3.4[N]+more than 0.05%), be limited to 3.4[N on preferably]+below 0.09% (more preferably 3.4[N]+below 0.08%).
[N：0.001～0.01％]
N is the element of inevitably sneaking into, and preferably reduces as far as possible, but reduces and have limit among actual process code, therefore taking 0.001% as lower limit.In addition, if N content surplus because strain aging causes ductility deteriorated, or is separated out as BN, make to improve effect from the hardenability of solid solution B and reduce, therefore using the upper limit as 0.01%.On N content preferred, be limited to (more preferably below 0.006%) below 0.008%.
Hot pressing of the present invention is described above by the basic chemical composition of steel plate, and surplus is the inevitable impurity (for example, O, H etc.) beyond iron and P, S.Use in steel plate in hot pressing of the present invention in addition, as required, also contain as also useful in inferior element: more than one that (a) select from the group that V, Nb and Zr formed: add up to (not containing 0%) below 0.1%; (b) more than one that select the group who forms from Cu, Ni, Cr and Mo: add up to (not containing 0%) below 1%; (c) more than one that select the group who forms from Mg, Ca and REM (rare earth element): add up to 0.01% below and (do not contain 0%), according to the kind of contained element, hot pressing is further improved by the characteristic of steel plate.Described in preferred scope while containing these elements and its circumscription be the reasons are as follows.
[more than one that select the group who forms from V, Nb and Zr: add up to 0.1% below and (do not contain 0%)]
The effect that V, Nb and Zr have is, forms fine carbide, utilizes pinning effect to make to organize fine.In order to bring into play such effect, preferably add up to and make it to contain more than 0.001%.But, if the content surplus of these elements forms thick carbide, become the starting point of fracture, make on the contrary ductility deteriorated.Set out thus, preferably these elements add up to below 0.1%.Under the content of these elements preferred, be limited to and add up to more than 0.005% (more preferably more than 0.008%), be limited to total (more preferably below 0.06%) below 0.08% on preferred.
[more than one that select the group who forms from Cu, Ni, Cr and Mo: add up to (not containing 0%) below 1%]
Cu, Ni, Cr and Mo suppress ferrite transformation and pearlitic transformation, therefore, in cooling after heating, prevent the formation of ferrite, perlite, bainite, to guaranteeing that retained austenite plays a role effectively.In order to bring into play such effect, preferably add up to and make it to contain more than 0.01%.If only consideration characteristics, the many methods of preferred content, but the angle that the cost adding from alloy rises is preferably and adds up to below 1%.In addition, because have the effect that significantly improves austenitic intensity, so that the load of hot rolling becomes is large, the manufacture of steel plate becomes difficulty, so from the viewpoint of manufacturing, be also preferably below 1%.Under these constituent contents preferred, be limited to and add up to more than 0.05% (more preferably more than 0.06%), be limited to total (more preferably below 0.3%) below 0.5% on preferred.
[more than one that select the group who forms from Mg, Ca and REM: add up to 0.01% below and (do not contain 0%)]
Because these elements make inclusion miniaturization, so ductility is improved and effectively played a role.In order to bring into play such effect, preferably add up to and make it to contain more than 0.0001%.If only consideration characteristics, the many situations of preferred content, but from the saturated angle of effect, be preferably and add up to below 0.01%.Under these constituent contents preferred, be limited to and add up to more than 0.0002% (more preferably more than 0.0005%), be limited to total (more preferably below 0.003%) below 0.005% on preferred.
In hot pressing of the present invention, with in steel plate, following 3 is also important important document: (A) contained containing among Ti precipitate in steel plate, and diameter of equivalent circle is that the average equivalent circular diameter containing Ti precipitate below 30nm is more than 3nm; (B) meet and separate out Ti amount (quality %)-3.4[N] > 0.5 × [total Ti content (quality %)-3.4[N]] relation [relation of described (1) formula]; (C) metal structure contains at least one of bainite and martensite, and the total of bainite and martensite point rate is more than 80 area %
If disperse imperceptibly in the steel plate of superfluous Ti before hot pressing with respect to N, or most exist with solid solution condition,, in the time of the heating of hot pressing, will exist in a large number with fine state.Like this, after heating, in the martensitic transformation occurring in the chilling in mould, martensite lath is hindered to the growth of lengthwise direction, is promoted to the growth of width, and long-width ratio diminishes thus.Consequently, discharge sluggishness from the carbon of the peripherad retained austenite of martensite lath, the carbon amount in retained austenite reduces, and the stability of retained austenite reduces, and therefore cannot fully obtain the raising effect of unit elongation.
From this viewpoint, need to make in advance to disperse containing Ti precipitate thickly, for this reason, contained containing among Ti precipitate in steel plate, the average equivalent circular diameter containing Ti precipitate that diameter of equivalent circle is 30nm need to be 3nm above [important document of above-mentioned (A)].Further, why the diameter of equivalent circle containing Ti precipitate as object being defined as below 30nm at this, is because need to be controlled at smelt stage forms thickly, has removed thereafter tissue changes and characteristic can not impact TiN to contain Ti precipitate.Containing the size (diameter of equivalent circle is the average equivalent circular diameter containing Ti precipitate below 30nm) of Ti precipitate, more than being preferably 5nm, more preferably more than 10nm.Further, in so-called the present invention as object containing Ti precipitate, the meaning is except TiC and TiN, also comprises the precipitate that contains Ti of TiVC, TiNbC, TiVCN, TiNbCN etc.
In addition,, need to make among Ti for separating out most existing with precipitation state of Ti beyond fix N with in steel plate in hot pressing.For this reason, the Ti amount that exists as the precipitate beyond TiN (separate out Ti amount (quality %)-3.4[N]), need for than deducting Ti remaining that forms TiN more than 0.5 times (, than 0.5 × [total Ti content (quality %)-3.4[N]] many) [important document of above-mentioned (B)] among total Ti.Separate out Ti amount (quality %)-3.4[N] be preferably 0.6 × [total Ti content (quality %)-3.4[N]] more than, more preferably 0.7 × [total Ti content (quality %)-3.4[N]] more than.
Metal structure was the needed control of intensity-unit elongation balance of reaching expectation in molding originally, but can not, only with hot pressing condition control metal structure, also need to control in advance for organizing of this raw steel (hot pressing steel plate).In shaping steel plate, in order to guarantee in right amount fine and ductility to be contributed to large annealing martensite and annealing bainite, the total point rate that need to make the bainite and martensite in steel plate is more than 80 area %.If the total of bainite and martensite divides rate lower than 80 area %, be difficult to guarantee annealing martensite and/or the annealing bainite point rate of expection, make in addition other tissue (for example, ferrite) amount increase, will make strength-ductility balanced reduction.The total of bainite and martensite is divided rate, more than being preferably 90 area %, more preferably more than 95 area %.
Further, in hot pressing of the present invention, with in steel plate, the surplus of metal structure is not particularly limited, but for example can enumerate ferrite, perlite or retained austenite at least any one.
In order to manufacture above-mentioned such steel plate of the present invention (hot pressing steel plate), making Heating temperature is 1100 DEG C above (being preferably more than 1150 DEG C) and 1300 DEG C following (below being preferably 1250 DEG C), finishing temperature is 750 DEG C above (being preferably more than 780 DEG C) and 850 DEG C following (below being preferably 830 DEG C), melting is had to the slab that the steel of above-mentioned such chemical composition composition form and carry out hot rolling, 700～750 DEG C (be preferably 720～740 DEG C) between make it stop and more than 10 seconds (be preferably more than 50 seconds) and carry out after cooling (Xu Leng: intercooling) thereafter, with 20 DEG C/sec of above (being preferably more than 30 DEG C/sec) cooling (chillings) to (being preferably below 350 DEG C) below 450 DEG C, and more than 100 DEG C, (be preferably more than 150 DEG C) and (be preferably below 400 DEG C) and batch below 450 DEG C.
Aforesaid method is controlled as follows: the dislocation that (1) is imported by hot rolling in austenite also remaining temperature field finishes rolling; (2) Xu Leng immediately thereafter immediately makes forming containing Ti precipitate of TiC etc. in dislocation thickly; (3) again by batching after chilling, make it to occur bainitic transformation or martensitic transformation.
There is the hot pressing steel plate of above-mentioned such chemical composition composition, metal structure and Ti precipitation state, can be directly for the manufacture of hot pressing, also can be after pickling, with draft: 10～80% (being preferably 20～70%) are implemented cold rolling.In addition, also can be by steel plate or its cold rolling material for hot pressing, being heated to TiC does not have after the temperature range (for example, below 1000 DEG C: 870～900 DEG C) of all fusings, be chilled to after 450 DEG C following (below being preferably 400 DEG C) with the speed of cooling of 20 DEG C/sec above (being preferably more than 30 DEG C/sec), be implemented in 450 DEG C of following maintenances more than 10 seconds, below 1000 seconds, or implement the such thermal treatments of tempering with 450 DEG C of following temperature.In addition, hot pressing of the present invention also can implement to contain more than one the plating among Al, Zn, Mg, Si to its surface (matrix surface of steel plate) with steel plate.
Use above-mentioned such hot pressing steel plate, be heated to A c1transformation temperature+20 DEG C above and A c3after DEG C following temperature of transformation temperature-20, start stamping, after the neutralization that is shaped is shaped and finishes, in mould, guarantee more than 20 DEG C/sec average cooling rates on one side, be cooled to than bainitic transformation and start below the temperature of low 100 DEG C of temperature Bs on one side, thus, there are the stamping product of single characteristic (below, have the situation that is called single area molding) in, can produce the best tissue as low strength and high ductibility.Described in the regulation of each important document of this moulding method be the reasons are as follows.
For the lath chien shih austenitic formation of the martensite in steel plate and bainite, and martensite and bainite are annealed, thereby form the annealing martensite of ductility excellence and the bainite of annealing, Heating temperature need to be controlled at the scope of regulation.If the Heating temperature of steel plate is lower than A c1transformation temperature+20 DEG C, can not get the fully austenite of amount while heating, can not in final tissue (tissue of molding), guarantee the retained austenite of specified amount.In addition, if the Heating temperature of steel plate exceedes A c3transformation temperature-20 DEG C, excessively increase to austenitic phase variable while heating, can not in final tissue (tissue of molding), guarantee annealing martensite and the annealing bainite of specified amount.
In order to stop the generation of the tissue of ferrite or perlite etc. on one side, make the austenite forming in above-mentioned heating process become the tissue of expectation on one side, need suitably control to be shaped and be neutralized into average cooling rate and the cooling end temp after shape.From this viewpoint, it is more than 20 DEG C/sec needing the average cooling rate in being shaped, and cooling end temp is to start below the temperature of low 100 DEG C of temperature Bs than bainitic transformation.Average cooling rate in shaping is preferably 30 DEG C/sec above (more preferably more than 40 DEG C/sec).Be that bainitic transformation starts below temperature Bs by making cooling end temp, thereby stop the generation of the tissue of ferrite or perlite etc. on one side, in the time of heating, make the austenite phase transformation existing become bainite and martensite on one side, guarantee on one side thus bainite and martensite, between the lath of bainite and martensite, make fine austenite residual and guarantee the retained austenite of specified amount on one side.
Above-mentioned cooling end temp is higher than the temperature that starts low 100 DEG C of temperature Bs than bainitic transformation, or average cooling rate is during lower than 20 DEG C/sec, form the tissue of ferrite and pearlite etc., can not guarantee the retained austenite of specified amount, the unit elongation (ductility) of molding is deteriorated.
In the temperature stage below the temperature in start low 100 DEG C of temperature Bs than bainitic transformation, do not need the control of average cooling rate substantially, and also for example average cooling rates above with 1 DEG C/sec, below 100 DEG C/sec are cooled to room temperature.Further, the be shaped control of the average cooling rate after finishing of the neutralization that is shaped, can be by reaching as inferior means: (a) temperature of control shaping dies (as described in Fig. 1 as shown in heat-eliminating medium); (b) thermal conductivity of control mould.
In the stamping product of manufacturing by above-mentioned such hot pressing, metal structure is, retained austenite: 3～20 area %, annealing martensite and/or annealing bainite: 30～87 area %, as-quenched condition martensite: 10～67 area %, and the carbon amount in described retained austenite is more than 0.60%, can also in molding, reach using high level the balance of high strength and unit elongation as uniform characteristic.The scope of each important document (the carbon amount in standard weave and retained austenite) of such hot compacting product is set and be the reasons are as follows.
Retained austenite becomes mutually martensite in viscous deformation, makes work hardening rate increase (phase change induction plasticity), has the effect that the ductility of stamping product is improved.In order to bring into play such effect, it is more than 3 area % need to making retained austenite point rate.For ductility, as long as retained austenite divides rate many, The more the better.At the composition for automotive sheet, the retained austenite that can guarantee is limited, and 20 area % left and right are the upper limit.The preferred lower limit of retained austenite is 5 area % above (more preferably more than 7 area %).
Be annealing martensite fine and that dislocation desity is low and/or annealing bainite by making Main Tissues, can guarantee the intensity of regulation on one side, improve the ductility (unit elongation) of stamping product on one side.From this viewpoint, point rate of annealing martensite and/or annealing bainite is more than 30 area %.But, if its point of rate exceedes 87 area %, the point rate deficiency of retained austenite, ductility (residual ductility) reduces.Under point rate of annealing martensite and/or annealing bainite preferred, be limited to 40 area % above (more preferably more than 50 area %), be limited to lower than 80 area % (more preferably lower than 70 area %) on preferably.
As-quenched condition martensite is the tissue that lacks ductility, if therefore exist in a large number, make unit elongation deteriorated, but in order to be to realize 100 kilograms of (キ ロ) super high strength in the tissue that intensity is low at matrix, need to guarantee as-quenched condition martensite with specified amount as annealing martensite.From this viewpoint, martensitic point of rate of as-quenched condition is more than 10 area %.But if martensitic point of rate of as-quenched condition is too much, intensity becomes too high, unit elongation is by deficiency, and therefore its point of rate need to be below 67 area %.Under martensitic point of rate of as-quenched condition preferred, be limited to 20 area % above (more preferably more than 30 area %), be limited to 60 area % following (more preferably 50 area % are following) on preferred.
Except above-mentioned tissue, can also contain ferrite, perlite and bainite etc. as surplus tissue, but these tissues, for the contribution of intensity and lower than organizing of other for the contribution of ductility, preferably do not contain (can be also 0 area %) substantially.But, can allow by the end of 20 area %.Surplus is organized more preferably below 10 area %, more preferably below 5 area %.
Carbon amount in retained austenite, having influence in the time of the distortion of tension test etc. retained austenite processing brings out and is phase-changed into the martensitic moment, carbon amount is more, more in high strain domain, processing occurs and brings out phase transformation, has strengthened thus phase change induction plasticity (TRIP) effect.When processing treatment of the present invention, cooling in, carbon is discharged from the peripherad austenite of formed martensite lath.At this moment, if the Ti carbide or the carbonitride that are dispersed in steel disperse thickly, martensite lath makes progress in the clear to the growth of lengthwise direction, therefore becomes width long and narrow, the martensite lath that long-width ratio is large.Consequently, carbon is easily discharged from martensite lath broad ways, and the carbon amount in retained austenite increases, and ductility improves.From this viewpoint, in stamping product of the present invention, the carbon gauge in the retained austenite in steel is decided to be more than 0.60%.Further, the carbon amount in retained austenite can multiviscosisty to 0.70% left and right, but 1.0% left and right is boundary.
If use hot pressing steel plate of the present invention, by suitably adjusting stamping condition (Heating temperature and speed of cooling), can control the characteristic of intensity and the unit elongation etc. of stamping product, and can obtain the stamping product of high ductibility (residual ductility), therefore the stamping product that also go for up to now (are for example difficult to applicable position, energy-absorbing member), exceedingly useful in the scope of application that expands hot compacting product.In addition, be not only above-mentioned single area molding, and to use press forming die to carry out steel plate stamping and while manufacturing stamping product, if the condition in the each region when suitably controlling Heating temperature and being shaped, and adjust the tissue in each region, also can obtain having given play to the strength-ductility balanced stamping product corresponding with each region (following, to have the situation that is called multizone molding).
Use hot pressing steel plate of the present invention, while manufacturing as described so multizone molding, the heating region of steel plate is at least divided into 2 regions, one of them region (following, to be called first area) is heated to A c3temperature more than transformation temperature and below 950 DEG C, and another region (following, to be called second area) is heated to A c1transformation temperature+20 DEG C above and A c3after DEG C following temperature of transformation temperature-20, start stamping for first and second these two regions, after the neutralization shaping that is shaped finishes, in first and second any one regions, be all in mould, to guarantee more than 20 DEG C/sec average cooling rates on one side, being cooled to martensitic transformation starts the temperature below temperature Ms on one side.
In aforesaid method, the heating region of steel plate is divided into 2 regions (territory, high strength lateral areas and territory, low strength lateral areas), create conditions by corresponding regional control, can obtain having given play to and the corresponding strength-ductility balanced stamping product in each region.Among 2 regions, second area is equivalent to territory, low strength lateral areas, and the creating conditions of this region, tissue are substantially identical with above-mentioned single area molding with characteristic.Below, just the creating conditions of first area (being equivalent to territory, high strength lateral areas) that is used to form this side described.Also have, in the time implementing this manufacture method, be created in the needs that form the region that Heating temperature is different in single steel plate, but for example, by (using existing process furnace, far infrared stove, electric furnace+shield cap), the boundary member that can make temperature is that 50mm is following while control.
(creating conditions of territory, high strength lateral areas, first area)
In order suitably to adjust the tissue of stamping product, Heating temperature need to be controlled at the scope of regulation.By suitably controlling this Heating temperature, in process of cooling thereafter, can guarantee the retained austenite of specified amount on one side, make it to become mutually the tissue taking martensite as main body on one side, in the region of final hot compacting product, produce the tissue of expectation.If the steel plate Heating temperature in this region is lower than A c3transformation temperature, can not get the fully austenite of amount while heating, can not guarantee the retained austenite of specified amount in final tissue (tissue of molding).In addition, if the Heating temperature of steel plate exceedes 950 DEG C, while heating, austenitic particle diameter becomes large, and martensitic transformation starts temperature (Ms point) and martensitic transformation finishing temperature (Mf point) rises, when quenching, retained austenite can not be guaranteed, good plasticity cannot be reached.The Heating temperature of steel plate is preferably A c3transformation temperature+50 DEG C are above and below 900 DEG C.
In order to stop the generation of the tissue of ferrite or perlite etc. on one side, make the austenite forming by above-mentioned heating process become the tissue of expectation on one side, need suitably control to be shaped and be neutralized into average cooling rate and the cooling end temp after shape.From this viewpoint, it is more than 20 DEG C/sec needing the average cooling rate in being shaped, and cooling end temp is that martensitic transformation starts below temperature (Ms point).Average cooling rate in shaping is preferably 30 DEG C/sec above (more preferably more than 40 DEG C/sec).Be that martensitic transformation starts below temperature (Ms point) by making cooling end temp, thereby stop the generation of the tissue of ferrite or perlite etc. on one side, in the time of heating, make the austenite phase transformation existing become martensite on one side, guarantee thus martensite.Cooling end temp is, below 400 DEG C, to be preferably below 300 DEG C specifically.
In the stamping product that obtained by this method, in first area and second area, the differences such as metal structure and precipitate.In first area, in metal structure, retained austenite: 3～20 area % (action effect of retained austenite is with above-mentioned), martensite: more than 80 area %.At second area, the carbon amount meeting in metal structure, the retained austenite identical with above-mentioned single area molding is more than 0.60%.
Make the Main Tissues of first area, become the high-intensity martensite of the retained austenite that contains specified amount, can guarantee ductility and the high strength of the specific region of stamping product.From this viewpoint, martensitic integration rate need to be more than 80 area %.Martensitic point of rate is preferably 85 area % above (more preferably more than 90 area %).Further, as the tissue of first area, also can partly contain ferrite, perlite, bainite etc.
Below, more specifically show effect of the present invention by embodiment, but following embodiment can not limit the present invention, carry out being all included in technical scope of the present invention of design alteration according to the forward and backward aim of stating.
[embodiment]
[embodiment 1]
Vacuum melting has the steel (steel No.1～32) of chemical composition shown in following table 1 composition, becomes experiment with after slab, carries out hot rolling and becomes steel plate, cooling and implement the processing (thickness of slab: 3.0mm) that simulation is batched thereafter.About batching simulation process method, be cooled to after coiling temperature, in the stove that is heated to coiling temperature, put into sample, keep carrying out after 30 minutes stove cold.At this moment steel plate is created conditions and is presented in following table 2.Further, the A in table 1 c1transformation temperature, A c3transformation temperature, Ms point and Bs point, use following (2) formula～(5) formula to try to achieve (for example, " Lesley's iron steel " ball is kind, with reference to (1985)).In addition, the processing shown in the remarks column of table 2 (1)～(3), are to carry out the each processing (rolling, cooling, alloying) shown in following.
A c1transformation temperature (DEG C)=723+29.1 × [Si]-10.7 × [Mn]+16.9 × [Cr]-16.9[Ni] ... (2)
A c3transformation temperature (DEG C)=910-203 × [C] 1/2+ 44.7 × [Si]-30 × [Mn]+700 × [P]+400 × [Al]+400 × [Ti]+104 × [V]-11 × [Cr]+31.5 × [Mo]-20 × [Cu]-15.2 × [Ni] ... (3)
Ms point (DEG C)=550-361 × [C]-39 × [Mn]-10 × [Cu]-17 × [Ni]-20 × [Cr]-5 × [Mo]+30 × [Al] ... (4)
Bs point (DEG C)=830-270 × [C]-90 × [Mn]-37 × [Ni]-70 × [Cr]-83 × [Mo] ... (5)
Wherein, [C], [Si], [Mn], [P], [Al], [Ti], [V], [Cr], [Mo], [Cu] and [Ni] represent respectively the content (quality %) of C, Si, Mn, P, Al, Ti, V, Cr, Mo, Cu and Ni.In addition, during containing element shown in above-mentioned (2) formula～(5) formula every, remove this and calculate.
Process (1): after finish to gauge, be cooled to after 650 DEG C with the average cooling rate of 50 DEG C/sec, since cooling 10 seconds of 650 DEG C of average cooling rates with 5 DEG C/sec, be cooled to coiling temperature with 50 DEG C/sec of average cooling rates thereafter.Afterwards, in order to make thickness of slab and processing (2), (3) consistent, grind for table, the back side, subtract thick in 1.6mm.
Process (2): for hot-rolled steel sheet carry out cold rolling after, simulation continuous annealing, be heated to after 860 DEG C, with the average cooling rate of 30 DEG C/sec be cooled to 400 DEG C and keep.
Process (3): for hot-rolled steel sheet carry out cold rolling after, in order to simulate continuous fusion galvanizing line, be heated to, after 860 DEG C, be cooled to 400 DEG C with the average cooling rate of 30 DEG C/sec, after maintenance, carry out after reheating 500 DEG C × 10 seconds cooling.
[table 1]
[table 1]
[table 2]
For the steel plate obtaining, carry out the analysis of precipitation state and the observation of metal structure (point rate of each tissue) of Ti by following main points.By its result and 0.5 × [total Ti content (quality %)-3.4[N]] calculated value [be expressed as 0.5 × (total Ti content-3.4[N])] together be presented in following table 3.
[analysis of the precipitation state of the Ti of steel plate]
Make extraction replica sample, take the transmission electron microscope picture (multiplying power: 100,000 times) containing Ti precipitate with transmission electron microscope (TEM).At this moment, carry out the compositional analysis of precipitate by energy dispersion type x-ray spectrometer (EDX), specific for Ti precipitate thus.Measure at least 100 above areas containing Ti precipitate by image analysis, extracting diameter of equivalent circle is below 30nm, using its mean value as precipitation size.Further, in table, be expressed as " containing the average equivalent circular diameter of Ti precipitate ".In addition, separate out Ti amount (quality %)-3.4[N] (the Ti amount existing with precipitate form), use sieve diameter: the screen cloth of 0.1 μ m extracts residue analysis (when extraction process, precipitate aggegation, also can measure fine precipitate), try to achieve and separate out Ti amount (quality %)-3.4[N] (in table 3, be expressed as and separate out Ti amount-3.4[N]).Further, while containing V and Nb containing Ti precipitate part, also measure for its content.
[observation (point rate of each tissue) of metal structure]
(1), about the martensite in steel plate, the tissue of bainite, corrodes steel plate with nital, observe by SEM (multiplying power: 1000 times or 2000 times), distinguish martensite, bainite, tries to achieve point rate (area occupation ratio) separately.
(2) retained austenite in steel plate divides rate, is to be ground to after 1/4 thickness of steel plate, carries out chemical grinding, afterwards by X-ray diffraction method measure (for example, ISJJ Int.Vol.33. (1933), No.7, P.776).
[table 3]
For above-mentioned each steel plate (1.6mm t× 150mm × 200mm) (for above-mentioned processing (1)～(3) steel plate in addition, by hot rolling, thickness is adjusted to 1.6mm), be heated to process furnace after the temperature of regulation, implement stamping and cooling process with the mould (described Fig. 1) of cap shape, as stamping product.Stamping condition (Heating temperature when stamping, average cooling rate, rapidly cooling end temp) is presented in following table 4.
[table 4]
[table 4]
For obtained molding, measure the observation (point rate of each tissue) of tensile strength (TS), unit elongation (breaking elongation EL), metal structure with following method.
[measurement of tensile strength (TS) and unit elongation (breaking elongation EL)]
Use JIS5 test film to carry out tension test, measure tensile strength (TS), unit elongation (EL).Time, the rate of straining of tension test is 10mm/ second.In the present invention, tensile strength (TS) meets 980～1179MPa, and unit elongation (EL) meets more than 20%, and intensity-unit elongation balance (TS × EL) is 24000 (MPa%) when above, and it is qualified to be evaluated as.
[observation (point rate of each tissue) of metal structure]
(1) about the tissue of the annealing martensite in steel plate, bainite, annealing bainite, corrode steel plate with nital, observe by SEM (multiplying power: 1000 times or 2000 times), distinguish annealing martensite, bainite, annealing bainite, try to achieve point rate (area occupation ratio) separately.
(2) dividing rate about the retained austenite in steel plate, is to be ground to after 1/4 thickness of steel plate, carries out chemical grinding, afterwards by X-ray diffraction method measure (for example, ISJJ Int.Vol.33. (1933), No.7, P.776).At this moment, also measure for the carbon amount in retained austenite.
(3) divide rate about as-quenched condition martensite, that steel plate is carried out to the corrosion of lepera reagent, mixed structure using white contrast gradient place as as-quenched condition martensite and retained austenite, survey area rate, from wherein deducting the retained austenite point rate of trying to achieve by X-ray diffraction, calculate as-quenched condition martensite and divide rate.
The observations (point rate of each tissue) of metal structure is presented in following table 5.In addition, the mechanical characteristics of molding (tensile strength TS, unit elongation EL and TS × EL) is presented in following table 6.
[table 5]
[table 6]
Can be investigated as follows by these results.Steel No.1,2,4,5,11～13,15～17,19～21,23～32nd, meets the embodiment of important document given to this invention, the known good part that can obtain intensity-ductility balance.
With respect to this, steel No.3,6～10,14,18, the 22nd, the comparative example of discontented foot a certain important document given to this invention, a certain deterioration in characteristics.That is, steel No.3 has used the poor steel plate of Si, cannot guarantee the retained austenite point rate in molding, and the carbon amount in retained austenite reduces in addition, can not get unit elongation.Heating temperature when its shaping of steel No.6 is high, can only obtain low elongation EL, and intensity-unit elongation balance (TS × EL) is also deteriorated.
Its average cooling rate when stamping of steel No.7 is slow, and perlite and ferrite generate, and can not guarantee as-quenched condition martensite point rate, and intensity-unit elongation balance (TS × EL) is deteriorated.Steel No.8 its cooling end temp is high rapidly, generate perlite or ferrite and can not guarantee as-quenched condition martensite point rate, can only obtain low elongation EL, intensity-unit elongation balance (TS × EL) is also deteriorated.
Steel No.9,10 its conditions in the time that steel are manufactured are improper, separate out Ti quantity not sufficient (steel No.9,10), containing Ti precipitate little (steel No.10), use such steel plate to carry out when stamping, even if molding condition is suitable, intensity-unit elongation balance (TS × EL) is still deteriorated.
Steel No.14 has used because coiling temperature causes the example of metal structure for the steel plate of ferrite+perlite 100 area %, can not guarantee annealing martensite and/or annealing bainite point rate in molding, intensity-unit elongation balance (TS × EL) is deteriorated.Steel No.18 has used the steel plate of C content surplus, and intensity is high, can only obtain low elongation EL.Steel No.22 has used the steel plate of Ti content surplus, and intensity-unit elongation balance (TS × EL) is deteriorated.
[embodiment 2]
Vacuum melting has the steel (steel No.33～37) of chemical composition shown in following table 7 composition, becomes experiment with after slab, carries out hot rolling, cooling and batch (thickness of slab: 3.0mm) thereafter.At this moment steel plate is created conditions and is presented in following table 8.
[table 7]
[table 8]
For obtained steel plate, contain similarly to Example 1 the analysis of precipitation state and the observation of metal structure (point rate of each tissue) of Ti precipitate.Its result is presented in following table 9.
[table 9]
For above-mentioned each steel plate (3.0mm t× 150mm × 200mm), be heated to process furnace, after the temperature of regulation, implement stamping and cooling process with the mould (described Fig. 1) of cap shape, make molding.At this moment, steel plate is put into infrared heating heating furnace, for the part (being equivalent to the steel plate part of first area) of wanting high strength, can carry out the mode infrared rays direct irradiation of heat, want the part (being equivalent to the steel plate part of second area) of low strength simultaneously, can carry out the mode of low-temperature heat, cover overcover to interdict a ultrared part, thereby it is poor to give Heating temperature.Therefore, molding has the region that intensity is different in single part.Stamping condition (Heating temperature in the each region when stamping, average cooling rate, rapidly cooling end temp) is presented in following table 10.
[table 10]
For obtained molding, try to achieve similarly to Example 1 the carbon amount in observation (point rate of each tissue) and the retained austenite of tensile strength (TS), unit elongation (full unit elongation EL), metal structure in each region.
The observations (point rate of each tissue) of metal structure is presented in following table 11.In addition, the mechanical characteristics of molding (tensile strength TS, unit elongation EL and TS × EL) is presented in following table 12.Also have, meet the tensile strength (TS) of high strength side for more than 1470MPa, unit elongation (EL) is more than 8%, intensity-unit elongation balance (TS × EL) is 14000 (MPa%) when above, is evaluated as qualified (judgement criteria of low strength side is identical with embodiment 1).
[table 11]
[table 12]
Result can be investigated as follows thus.Steel No.33,35, the 37th, meets the embodiment of the important document specifying in the present invention, the good part of known intensity-ductility balance that can obtain each region.
Relatively therewith, steel No.34, the 36th, the comparative example of discontented foot a certain important document given to this invention, a certain deterioration in characteristics., its Heating temperature when stamping of steel No.34 is low, the strength decreased of high strength side.Steel No.36 has used the little steel plate of size containing Ti precipitate, can only obtain low strength in high strength side, deteriorated in low strength side intensity-unit elongation balance (TS × EL).
In detail and with reference to specific embodiment the present invention has been described, but can departed from the spirit and scope of the present invention and in addition various changes and amendment, this it will be apparent to those skilled in the art that.
The Japanese patent application (patent application 2012-053844) of the application based on March 9th, 2012 application, its content this with reference to and quote.
[utilizability in industry]
Hot pressing steel plate used when the present invention is suitable for manufacturing the structural parts of automobile.
[nomenclature]
1 drift
2 punch dies
3 blank holders
4 steel plates (base substrate)

Claims (6)

1. a hot pressing steel plate, is characterized in that, described steel plate does not contain following chemical composition composition with quality % score,
C：0.15～0.5％、
Si：0.2～3％、
Mn：0.5～3％、
P:0.05% following and containing 0%,
S:0.05% following and containing 0%,
Al：0.01～1％、
B：0.0002～0.01％、
Ti:3.4[N]+more than 0.01%, 3.4[N]+below 0.1%, wherein, [N] represents the content in the N of quality %, and
N：0.001～0.01％，
Surplus is made up of iron and inevitable impurity;
Contained containing among Ti precipitate in steel plate, diameter of equivalent circle is that the average equivalent circular diameter containing Ti precipitate below 30nm is more than 3nm, and the Ti amount of separating out in steel and total Ti content meet the relation of following (1) formula, and the total of the bainite and martensite in metal structure divides rate more than 80 area %
Separate out Ti amount-3.4[N] > 0.5 × [total Ti content-3.4[N]] ... (1)
(1), in formula, [N] represent in the content of the N in the steel of quality %, described in separate out Ti amount and described total Ti content all in quality %.
2. hot pressing steel plate according to claim 1, wherein, also contains following (a) using quality %～at least 1 element as other (c):
(a) more than one that select the group who forms from V, Nb and Zr: add up to 0.1% below and not and contain 0%;
(b) more than one that select the group who forms from Cu, Ni, Cr and Mo: add up to below 1% and not containing 0%;
(c) more than one that select the group who forms from Mg, Ca and REM: add up to 0.01% below and not and contain 0%.
3. a manufacture method for stamping product, is characterized in that, right to use requires the hot pressing steel plate described in 1 or 2, is heated to A c1transformation temperature+20 DEG C above and A c3after the following temperature in transformation temperature-20 DEG C, start stampingly, after the neutralization that is shaped is shaped and finishes, guarantee more than 20 DEG C/sec average cooling rates in mould on one side, one side is cooled to start below the temperature of low 100 DEG C of temperature Bs than bainitic transformation.
4. stamping product, the stamping product that obtained by manufacture method claimed in claim 3, it is characterized in that, in metal structure, retained austenite: 3～20 area %, annealing martensite and/or annealing bainite: the martensite of 30～87 area %, as-quenched condition: 10～67 area %, and carbon amount in described retained austenite is more than 0.60%.
5. a manufacture method for stamping product, is characterized in that, right to use requires the hot pressing steel plate described in 1 or 2, and the heating region of steel plate is divided into 2 regions, and one of them region is heated to A c3temperature more than transformation temperature and below 950 DEG C, and another region is heated to A c1transformation temperature+20 DEG C above and A c3after the following temperature in transformation temperature-20 DEG C, start stampingly, after the neutralization that is shaped is shaped and finishes, guarantee more than 20 DEG C/sec average cooling rates in mould on one side, one side is cooled to martensitic transformation and starts the temperature below temperature Ms.
6. stamping product, be the stamping product that obtained by manufacture method claimed in claim 5, it is characterized in that, there is first area and second area, in described first area, the retained austenite of metal structure is that 3～20 area %, martensite are more than 80 area %; In described second area, the retained austenite of metal structure is that 3～20 area %, annealing martensite and/or annealing bainite are that 30～87 area %, as-quenched condition martensite are 10～67 area %, and carbon amount in described retained austenite is more than 0.60%.
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