GB2452230A - High-strength composite steel sheet having excellent moldability and delayed fracture resistance - Google Patents
High-strength composite steel sheet having excellent moldability and delayed fracture resistance Download PDFInfo
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- GB2452230A GB2452230A GB0900057A GB0900057A GB2452230A GB 2452230 A GB2452230 A GB 2452230A GB 0900057 A GB0900057 A GB 0900057A GB 0900057 A GB0900057 A GB 0900057A GB 2452230 A GB2452230 A GB 2452230A
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- ferrite
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- polygonal ferrite
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 61
- 239000010959 steel Substances 0.000 title claims abstract description 61
- 239000002131 composite material Substances 0.000 title claims abstract description 19
- 230000003111 delayed effect Effects 0.000 title abstract description 10
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 14
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 12
- 239000000126 substance Substances 0.000 claims abstract description 9
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 229910001568 polygonal ferrite Inorganic materials 0.000 claims description 48
- 229910000859 α-Fe Inorganic materials 0.000 claims description 45
- 229910001566 austenite Inorganic materials 0.000 claims description 9
- 239000000203 mixture Substances 0.000 abstract description 3
- 239000002184 metal Substances 0.000 description 24
- 229910052751 metal Inorganic materials 0.000 description 24
- 238000000137 annealing Methods 0.000 description 21
- 238000012360 testing method Methods 0.000 description 20
- 230000000694 effects Effects 0.000 description 19
- 239000000463 material Substances 0.000 description 18
- 238000001816 cooling Methods 0.000 description 17
- 238000010438 heat treatment Methods 0.000 description 15
- 230000015572 biosynthetic process Effects 0.000 description 14
- 229910001563 bainite Inorganic materials 0.000 description 9
- 230000006866 deterioration Effects 0.000 description 6
- 238000000034 method Methods 0.000 description 6
- 238000010791 quenching Methods 0.000 description 6
- 230000000171 quenching effect Effects 0.000 description 6
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 230000002708 enhancing effect Effects 0.000 description 5
- 229910052739 hydrogen Inorganic materials 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000001737 promoting effect Effects 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 230000002411 adverse Effects 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 230000001965 increasing effect Effects 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 238000001000 micrograph Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- 241000357701 Polygona Species 0.000 description 1
- 101001012040 Pseudomonas aeruginosa (strain ATCC 15692 / DSM 22644 / CIP 104116 / JCM 14847 / LMG 12228 / 1C / PRS 101 / PAO1) Immunomodulating metalloprotease Proteins 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 235000018936 Vitellaria paradoxa Nutrition 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 230000037396 body weight Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- MWUXSHHQAYIFBG-UHFFFAOYSA-N nitrogen oxide Inorganic materials O=[N] MWUXSHHQAYIFBG-UHFFFAOYSA-N 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
Classifications
-
- 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
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
-
- 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
- C22C38/38—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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Landscapes
- 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
Disclosed is a high-strength composite steel sheet having a tensile strength of 980 MPa or greater and excellent in moldability, delayed fracture resistance and spot weldability. The steel sheet comprises a steel having the following chemical composition: C: 0.12-0.25% Si: 1.0-3.0%, Mn: 1.5-3.0%, P: 0.15% or less, S: 0.02% or less, Al: 0.4% or less, and Cr: 1.0% or less, with the remainder being iron and unavoidable impurities, wherein the contents of Si, Al, Mn and Cr satisfy the relationship expressed by the following formula: (Si+Al)/Mn or (Si+Al)/(Mn+Cr)=0.74-1.26 and the steel sheet has a specified microstructure.
Description
DESCRIPTION
HIGH-STRENGTH COMPOSITE STEEL SHEET HAVING EXCELLENT
FORMABILITY AND ANTI-DELAYED FRACTION PROPERTY
TECHNICAL FIELD [0001
The present invention relates to a high-strength composite steel sheet which has a tensile strength of 980 MPa or higher class as well as excellent formability and excellent anti-delayed fractior.. property, and also has exceller.t spot-weldability and is useful as automotive structural parts (body flame members such as pillar, member and reinforcement; bumper, doorguardbar, sheetparts, suspensionparts, andother reinforcing members)
BACKGROUND ART
[0002) In recent years, for the purpose of reducing ftel consumotion due to saving body weight of automobiles and ensuring safety upon collision, demands for high-strength steels have increased more and more. Accordingly, steel sheets having a tensile strength of 980 MPa or higher class have been required in place of those having a tensile strength of 590 MPa class. However, in the case of high-strength s:eel sheets having a tensile strength of 980 MPa or higher class, deterioration of formability cannot be avoided and there is restriction on applications since it is possible to apply to parts having complicated shapes.
[0003] In the case of high-strength steel sheets having a tensile strength of 980 NPa or higher class, residual stress generated upon press forming increases and thus a risk of delayed fracture enhances. That is, delayed fracture is a phenomenon in which hydrogen in the corrosion environment or atmosphere is diffused and accumulated at dislocations, vacancies and grain boundaries in the structure of steel materials, especially high-strength steel sheets thereby causing enibritt:ement of the materials, leading to fracture when stress is applied. Therefore, delayed fracture exerts a severe influence on ductility and toughness of steel materials. [00O4
Thus, it is very important to improve, in addition to the strength, formability (i.e. elongation and stretch flangeability) and anti-delayed fraction property so as to response to the above-described demand ot increasing the strength.
[0305) Now various steel sheets including residual austenite in the metal structure are put into practical use as high-strength steel sheets which exhibit excellent formability.
[0006] For example, Non-Patent Document 1 discloses a steel sheet in which a bore expansion property (i.e. stretch flangeability) is enhanced while ensuring a high strength by consituting the metal structure with a composite structure which mainly contains bainitic ferrite and also contains lath-tyoe residual austenite. However, when a tensile strength (TS) becomes a tensile strength of 980 NPa or higher class, this steel sheet shows TS x El as an indicator of the strength (TS) and dictility (El) of 9,0CC to 10,300 at most and therefore it is hardly to say that the steel sheet is satisfactory. 00C7]
It is considered that, in a mass production line of a practical operation using a continuous annealing furnace, a maximum heating temperature is about 900°C and a heating time is 5 minutes or less. However, under the production conditions disclosed in this document, it is required to cool to a temperature within the range from 330 to 400°C in a salt bath after annealing at 950°C for 1,200 seconds, and thus this method is not suited for the practical operation.
(0008] In Patent Document 1, elongation of about 20% and stretch flangeability (A) of 55% are attained while ensuring a tensile strength of 980 MPa or higher by constituting a matrix phase with a structure composed mainly of bainitic ferrite and 3% or more of residual austenite. However, in this technique, the addition of expensive alloy elements such as Mo, Ni and Cu is indispensable and it leaves a room for improvement in cost.
[0009] Furthermore, in Patent Document 2, high-leve. elongation and stretch flangeability are attained by constituting a matrix structure with tempered raartensite and ferrite and adjusting the occupancy ratio of residual austenite within the range from 5 to 30%. However, since a Inicrostructure before annealing is important so as to obtain the required metal structure using this technique, it is necessary to perform continuous annealing or annealing twice or more after incorporating a proper metal structure by ree.�ng up at low temPerature during a hot rolling step. However, in the case of reeling up at low temperature during the hot rolling step, since the structure before annealing is broken and the intended metal structure is not obtained unless the subsequent cold rolling reduction is controlled to the low value, severe restriction is added to the thickness and thickness tolerance. when continuous annealing is performed twice, although there is no restriction on the thickness, the numoer of steps increases when compared with the case of a conventional method and thus cost-up cannot be avoided.
[00102 Furthermore, Patent Docucrent 3 discloses steel sheets having enhanced total elongation and stretch flangeability by mainly constituting a matrix structure with tempered bainite.
However, since a study is mainly made on steels having a tensile strength of 900 MPa class in this steel type, delayed fracture, which is caused in steels having a tensile strength of 980 MPa or higher class, is not sufficiently studied.
on-PatenL Document 1: ISIJ International, Vol. 40 (2000), No. 9, pp. 920 to 926 Patent Document 1: Japanese Unexamined Patent Publication (Kokai) No. 2004-332099 Patent Document 2: Japanese Jnexamined Patent Publication (Kokai) No. 2003-171735 Patent Document 3: Japanese Unexamined Patent Publication (Kokai) No. 2002-309334
DISCLOSURE OF THE INVENTION
PROBLEMS TO BE SOLVED BY THE INVENTION
[0011] The present invention has been made in view of the above-mentioned prior arts, and an oblect thereof is to provide a high-strength composite steel sheet which has a tensile strength of 980 MPa class suited for use as automotive structural parts and has excellent formability (stretch flangeability), and also has excellent spot-weldability and excellent anti-delayed fraction property, without adding expensive alloying elements such as No, Ni and Cu.
MEANS FOR SOLVING THE PROBLEMS
:0012] The high-strength composite steel sheet of the present invention, which could achieve the above object, is a high-strength composite steel sheet having excellent formabi.ity and anti-delayed fraction property, comprising a steel satisfying C: 0.10 to 0.25%, Si: 1. 0 to 3.0%, Mn: 1.5 to 3.0%, P: 0.15% or less (excluding 0%), S: 0.02% or less(excluding 0%), Al: 3.4% or less (excluding 0%), and comprising a remnant made from iron and unavoidable impurities, wherein the contents of Si, Al and Mn satisfy the relationship of the following formula (I) (Si + A:j/Mn: 0.7' to 1.26 (I) or comprising a steel satisfying C: 0.12 to 0.25%, Si: 10 to 3.3%, Mn: 1.5 to 3.0%, Cr: 1.0% or less (excluding 0%), P: 0.15% or less (excluding 0%), 5: 0.02% or less (excluding 0%), Al: 0. 4% or less, and comprising a remnant made from iron and unavoidable impurities, wherein the contents of Si, Al, Mn and Cr satisfy the relationship of the following formula (II): (Si. + Al)/(Mn + Cr): 0.74 to 1.26 (Ii) and a microstructure in a longitudinal section comprises, by an occupancy rat.o based on the entire structure, 1) bainitic ferrite: 50% or more, 2) polygonal ferrite: 5 to 35%, 3) average grain size of polygonal ferrite: lopmor less], and 4) residual austenite: 5% or more.
[0013] The high-strength composite steel sheet of the present invention optionally con:ains, in addition to the above elements, Ti: 0.15% or less (excluding 0%) and/or Nb: 0.1% or less (excluding 0%), or optionally contains Ca: 30 ppm or less (excluding 0%) and/or REM: 30 ppm or less (excluding 0%) as other elements.
[0014] It is particularly preferred that the high-strength composite steel sheet of the present invention has a tensile strength of 980 MPa or higher so as to more effectively make use of its high strength.
EFFECT OF THE INVENTION
[00151 According to the present invention, by specifying chemical components of the steel material as described above, particularly controlling a ratio (Si + AU/Mn or a ratio (Si + Al)/(Mn + Cr), and constituting the metal strtcture with a cornposte structure which mainly contains bainitic ferrite (BF) and also contains polygonal ferrite (PF) and residual austenite (residual y), it is possible to provide a composite steel sheet which has good formability (elongation-stretch flangeability) and also excellent spot-wedability and anti-delayed fraction property while ensuring a tensile strength of 980 MPa or higher class at cheap price.
BRIEF DESCRIPTION OF THE DRAWINGS
[0016) Fig. 1 is a diagram for explaining a heat pattern of a heat treatment employed in Test Example.
BEST MODE FOP. CARRYING OUT THE INVENTION [3017] In light of the problems described above, the oresenc inventors have focused on a TRIP steel sheet (Transformation Induced Plasticity) having a tensile strength of 980 NPa or higher class, containing bairitic ferrite as a matrix phase, and intensively studied by paying attention to the form of the second phase in the metal structure and chemical components, especially Si, Al and Mn (and/or Cr) so as further improve formability, spot-weldability and anti-delayed fraction property. Thus, the following finings were obtained.
[00181 1) When a predetermined amount of fine polygonal ferrite is incorporated into a structure composed mainly of bainitic ferrite, elongation is remarkably improved. Moreover, when the ferrite to be incorporated is fine ferrite, deterioration ofthestrengthand stretch flangeabilityis suppressedandalso the structure exhibits excellent performances in anti-delayed fracture characteristics.
:0019] 2) When (Si � Al) and Mn or (Mn � Cr) among chemical components of the steel are adjusted so as to obtain a predetermined ratio, it is possible to obtain a desired structure having a tensile strength of 980 MPa or higher class while suppressing deterioration of spot-weldability.
[0020] Based on these findings, the present inventors have intensively studied about an influence of the contents of Si, Al, Mn and Cr in steel components and the metal structure on the strength, formability, spot-weldability and anti-delayed fracture characteristics. As a result, they have confirmed that a high-strength composite steel sheet having high performances, which achieve the above object, can be obtained by controlling the occupancy ratio of bainitic ferrite in the metal structure, controlling the occupancy ratios of polygonal ferrite and residual y and controlling an average grain size of the polygonal ferrite to a specific value or less using a steel material having specific component composition described above. Thus, the present invention has been completed.
[0021] Specific constitutions of the present irvention will be made clear by way of reasons for decision of chemical components of the steel material.
[0022] First, reasons for decision, of chemical components of the steel material are explained. [0023
C: 0.10% or more and 0.25% or less C is an element which is indispensable so as to ensure a high strength and residual y, and is an important element so as to incorporate a s,ifficient amount o C in a y phase thereby retaining a desired amount of the phase at room temperature.
In order co effectively exert such an effect, the content of C must be 0.10% or more, preferably 0.12% or more, and 0.15% or more. When the content of C is too large, a severe adverse influence is exerted on spot-weldability, and thus the upper limit was 0.25% in view of security of spot-weldability. The o content is preferably 0.23% or less, and more preferably 0.20% or less.
[0024] Si: 1.0 to 3.0% Si is an essential element which effectively serves as a solution-hardening element and also suppresses formation of a carbide as a result of decomposition of residual y. In order to effectively exert such an effect, the content of Si must be 1.0% or more, and preferably 1.2% or more. Since the effect is saturated at 3.0% and problems such as deterioration of spot-weldability and hot shortness arise when the content is more than the above value, the content may be suppressed to 3.0% or less, and preferably 2.5% or less.
[0025] Mn; 1.5 to 3.0% Mn is an element required to suppress formation of excess polygonal ferrite thereby forming a structure composed mainly of bainitic ferrite. Also it is an important element required to stabilize y thereby ensuring desired residual y. The occupancy ratio of Mn is at least 1.5% or more, and preferably 2.0% or more.
[0026] However, since excess addition causes deterioration of spot-weldability and anti-delayed fraction property, the content is suPpressed to 3.0% at most, and preferably 2.5% or less.
[0027] P: 0.15% or less, S: 0.32% or less These elements are inevitably incorporated into the stee and cause deterioration of formability and spot-weldability when the content increases, and thus the content must be suppressed to the upper limit or less.
�0028] Al: 0.4% or less Al is a useful element so as to suppress formation of a carbide thereby ensuring residual y similar to Si. However, if Al is too much, polygonal ferrite is likely to be produced; therefore, the content should be suppressed to 0.4% at most, and preferably 0.2% or less.
[0029] Cr: 1.0% or less Since Cr has the effect of suppressing formation of polygonal ferrite thereby enhancing the strength, it can be optionally added. However, when it is excessively added, an adverse influence may be exerted on formation of the target metal structure in the present invention. Therefore, the content should be suppressed to 1.0% at most.
[0030] (Si + Al)/Mn (or 4n + Cr): 0.74 to 1.26 (mass ratio) It is necessary to suppress excess formation of polygonal ferrire (PF) thereby promoting a bainitic ferrite (BF) transformation so as to obtain the intended metal structure in the present invention. Moreover, since C (carbon) discharged from bainitic ferrite is concentrated in a lath-type residual y, it is important to promote the bainitic ferrite transformation so as to obtain the lath-type residual y.
[0031] In the present invention, it is necessary to disperse an appropriate amount of fine ferrite in the metal structure. It was found that controlling a ratio of the content of Si and Al as ferrite formation promoting elements to Mn (or Mn + Cr) as ferrite formation suppressing elements so as to satisfy a given relation is extremely effective. Moreover, it was confirmed that controlling the content ratio of the ferrite formation promoting element/ferrite formation suppressing element is effective so as to enhance anti-delayed fraction property.
(0032] When the ratio (Si +Ai)/Mn (orMn� Cr) is less than 0.74, not only it becomes difficult to ensure a proper degree of polygonal ferrite, but also it becomes impossible to sufficiently ensuring bainitic ferrite. Moreover, C cannot be sufficiently concentrated in the residual y and stability of the residual y deteriorates and elongation deteriorates, and also the amount of martensite increases and stretch flangeability deteriorates.
[0033] Furthermore, anti-delayed fraction property is improved by controlling the ratio of the elements within a proper range.
Details of this reason are not sure, but are considered as follows. That is, Mn promotes delayed fracture by decreasing a grain boundary strength by grain boundary segregation and also promotes formation of voids serving as the starting point of delayed fracture upon working, whereas, Si and Al have the effect of increasing a tolerance amount of hydrogen which induces delayed fracture. Therefore, it is considered that anti-delayed fraction property varies by a ratio of both elements.
[03341 In contrast, when the ratio (Si + Al)/Mn (or Mn + Cr) exceeds 1.26, formation of polygonal ferrite is excessively prorro:ed and the occupancy ratio becomes excessive, and also the grain size of ferrite is likely to exceed 10 pm and thus both the strength and stretch flangeability deteriorate.
Further, since a ferrite grain boundary decreases when the ferrite grain size increases, anti-deiayed fraction property deteriorates. [0035
Therefore, it is important to adjust the component so as to control the ratio (Si + Al) /Mn (or Mn + Cr) within the range from 0.74 to 1.26, and more preferably 0.84 or more and 1.16 or less.
[0036] Nb: 0.1% or less, Ti: 0.15% or less Since these elements have the effect of enhancing toughness by refinement o the metal structure, these elements can be optionally added in a small amount. However, further effect is not obtained, to cause cost-up even if they are added in the amount of more than the upper limit, therefore it is wasteful.
[0037) Ca: 0.01% or less, REM: 0.01% or less Ca and REM have the effect of enhancing stretch flangeability by adding in a small amount and therefore they may be optionally added in a small amount. Since the effect is saturated at about 0.01%, it is wasteful even if they are added in a larger amount.
[0038J Mo, Cu, Ni: each about 0.1% or less These elements are effective for improving the strength and anti-delayed fraction property as described in the prior art. In the present invention, excellent performances are sufficiently obtained withou adding these elements and it is not necessary to add because these elements are expensive and.
cause cost-up. There is no restriction on the content ma level of impurities and these elements may be respectively added in the amount of about 0.1% or less. 0039)
Next, reasons of limitation of the metal tex:ure will be explained.
[0040) L6 3ainitic Ferrite �= 50% Bainitic ferrite has not only the effect of easily achieving a high strength because of somewhat high dislocation density, but also the effect of decreasing a difference in hardness between bainitjc ferrite and the second phase thereby enhancing stretch flangeability. Bainitic ferrite is a structure which is useful for enhancing anti-delayed fraction property. This reason is considered that bainitic ferrite does not contain or contains little cementite serving as the starting point of delayed structure, and has a high hydrogen absorbing effect because of a lot of dislocations. In order to effectively exert these effects, it is necessary that the content of bainitjc ferrite exist at 50% or more. The content is more preferably 60% or more.
COC41J The bainitic ferrite is different from a bainize structure in that the structure does not include carbides, and is also different from a polygonal ferrite structure having a lower bainite sLructure which does not contain or contains little dislocation, or a quasi-polygonal ferrite structure having a lower bainite structure such as fine subgrain. These differences can be easily identified by TEM (Transmission lectron Microscope) observation.
[0042J Polygonal Ferrite (PF) : 5 to 35% When a steel sheet having a tensile strength of 980 MPa or higher class, comprising bainite ferrite (BF) as a matrix phase contains a predetermined amount of polygonal ferrite having an average grain size described below, elongation is further improved. The content of polygonal ferrite must be contained at 5% or more so as to exert such an effect. However, since it becomes difficult to ensure the tensile strength and stretch flangeability when the content of polygonal ferrite is too large, the content should be suppressed to 35% at most.
Preferred occupancy ratio of polygona. ferrite is 10% or more and 30% or less.
[0043: Average Grain Size of Polygonal Ferrite: 10 pm or less The average grain size of polygonal ferrite must be 10 pm or less by the following reason. That is, refinement of ferrite enables uniform dispersion of the second phase, and thus both stretch flangeability and strength are enhanced and also anti-delayed fraction property is improved. This reason is considered that refinement of ferrite enables trap of hydrogen at the ferrite grain boundary and suppression of concentration of hydrogen at a dangerous site. The average grain size of polygonal ferrite as used herein means an average of an equivalent circle diameter (diameter of a cIrcle having the same area) of polygonal ferrite. 0C44]
Residual �= 5% Residual y has the effect o promoting hardening of the deformed part by transforming into inartensite when the material is deformedby application of strain, and thus preventing strain concentration (TRIP effect) . It is necessary that the content of the residual y is 5% or more so as Lo effectively exert such the effect. There is no restriction on the uper limit of the amount of the residual y. Since a large amount of C is required so as to form excessive residual y, 1: becomes difficult to reconcile with spot-weldabidity and workability, especially stretch flangeabili.ty. Therefore, the content is preferably suPpressed to about 30% or less.
[0045] In the composite steel sheet of the present invention, artensite, bainite and pearite can exist as the other balance structure. The contents of these other structures are preferably suppressed to 5% or less so as not to exert an adverse influence on the above operations and effects.
[0046] There is no noticeable restriction on the production conditions required to obtain the above metal structure defined in the present invention. In usual production procedures of a steel sheet, for example, cont1nuus casting, hot rolling, pickling, cold rolling and continuous annealing, a heating temperature, a heating rate, a holding temperature, a cooling initiation temperature and a cooling rate maybe properly controlled. In the case of a galvanized steel sheet and a gaivannealed steel sheet, proper temperature control including a continuous galvanizing line may be performed. Since heat treatment conditions in a continuous annealing line are most important so as to obtain the metal structure, preferred heat treatment conditions in he continuous annealing line will be mainly explained.
[0047] Heating Temperature upon Annealing: Ac3 + 10°C or higher in order to obtain the bainitic ferrite-riched metal structure, the heating temperature upon annealing may be adjusted to "Ac3 � 10°C or higher" so as to suppress formation of polygonal ferrite. By the way, when continuous annealing performed at an Ac3 point or lower, polygonal ferrite is likely to be formed in the subsequent cooling step since the residual ferrite serves as a nucleus, and thus it becomes difficult to obtain the intended metal structure in the present invention.
Therefore, more preferred heating temperature is "Ac3 + 30°C or higher".
[0048] Cooling Rate after Annealing The larger the cooling rate after annealing, the better since formation of polygonal ferrite is suppressed.
Considering equipment restriction and difficulty in temperature control, the cooling rate is preferably 25°C/sec or higher, and more preferably 30°C/sec or higher, so as to suppress the amount of polygonal ferrite to a certain amount of less according to each component system.
[0049] Quenching Termination Temperature after Annealing The tempera:ure at which quenching after annealing is terminated should be controlled to the temperature at which fine polygonal ferrite is formed or lower, and is preferably 650°C or lower, and more preferably 600°C or lower. When the quenching termination temperature becomes higher, coarse polygonal ferrite is formed and it becomes impossible to achieve the object of the present invention. However, since it becomes impossible to obtain a sufficient amount of polygonal ferrite when the quenching termination temperature becomes too low, the quenching termination temperature should be about 360°C or higher, and more preferably up to 400°C.
[0050] Holding Temperature after Cooling After coOling, since bainitic transformation proceeds by holding at a given temperature and also concentration of C to austenite proceeds to form residual y, it is important to properly control the holding temperature after cooling. The holding temperature is preferably within the range from 360 to 440°C so as to obtain the metal structure of the present 22.
invention. The retention time is preferably one minute or more.
It is necessary that the holding temperature is lower than the quenching termination temperature. After passing through the temperature range where fine ferrite is likely to be formed, 3 the material is transferred to a bainitic ferrite transformation temperature range.
[0051) in the high-strength composite steel sheet of the present invention, a composite steel sheet having a high strength of 980 MPa or higher class, good spot-weldabaility and anti-delayed fraction property can be provided at cheap price by using a steel material having specified chemical components as described above and employing proper heat treatment conditions including cooling conditions and holding conditions thereby ensuring a predetermined metal structure.
Examples
f 0052] The present invention is further illustrated by the foilowing examples. It is to be understood that the present invention is not limited to the examples, and various design variations made in accordance with the purports described hereinbe fore and hereinafter are also included in the technical scope of the present invention.
[0053]
Test Example
Steel materials with compositions shown in Table 1 were prepared, subjected to continuous casting, subjected to hot roiling and cold rolling under the conditions described below and then subjected to a heat treatment (annealing) under the conditions shown in Table 2 (also refer to Fig. 1) to obtain cold rolled steel sheets.
[0054] Hot Rolling] Heating temperaLure 1,200°C for 60 minutes Finish temoerature: 880°C Cooling: Cooling to 720°c at 40°C/sec, cooling for 10 seconds, cooling to 5C0°C at 40°C/sec and holding at 500°C for 60 minutes, followed by furnace cooling.
Finish thickness: 3.2 mm 10055] [Pickling, Cold Rolling] After pickling, cold rolling was performed to obtain a cold sheet having a thickness of 1.2 nzn.
[0056] [Heat Treatment (Annealing) As shown in Table 2, each cold rolled sheet was heated to a predetermined annealing temperature, held at the same temperature for 180 seconds, cooled to a predetermined cooling termination temperature at a predetermined cooling rate, held at a predetermined temperature for 6 minutes and then furnace-cooled. 0O57]
The metal structure of the resultant cold rolled steel sheet was confirmed by the following method and each test steel sheet was subjected to a tension test, a bore expansion test, a spot-welding test and an anti-delayed fracture test. The results collectively shown in Table 3 were obtained.
(0058] [Metal Structu:eJ Structure identification method A: Optical microscope observation (magnification: xl,030) by
repeller corrosion, 1 visual field
B: SEN observation (magnification: x4,000), 4 visual fields [0359) Polygonal Ferrite UT) Polygonal ferrite is identified by a micrograph taken by A described above. Since etched residual y and etched inartensite show a white color, whereas, etched PF shows a gray color, PF can be identified. After tracing the periphery of polygonal ferrite in the SEN micrograph taken by B described above, an equivalent circle diameter was calculated from the resultant trace image by image analysis. An average of the resultant equivalent circie diameter was taken as an average grain size of the polygonal ferrite.
[0060] Retained y, Martensite (H) and Bainite (B) After residual y, M and B were confirmed by a transition electzon microsc ope (TEM: magnification of x].5,000), the occupancy ratio was calculated from the micrograph taken by B described above.
[0061] Bainitic Ferrite (BF) After confirming that the structure is not a structure of bainite or pseudo-ferrite by a transition electron microscope (TEM: magnification of x15, 000), the occupancyratio was calculated by subtracting an amount of polygonal ferrite, an amount of residual y, and balance of martensite (M) and bainite (B) from 100%.
[0062] [Performance Evaluation Test] Tension test: The measurement was performed using JIS No. 5 tension test specimens.
Bore expansion test: The test was performed in accordance with the Japan Iron and Steel Federation Standard (JFST) 1001.
Spot-weldability: Spot-welding was performed under the following conditions. The case where a ductility ratio at a nugget diameter of 51t is 0.25 or more was rated Good (0) [0063] <Welding Conditions> Thickness of test material: 1.2 mm Electrode: Dome radius tyDe (tip diameter: 6 mm) Pressure: 375 kg tJpslope: icycle, electrification time: 12 cycles, hold: icycle (60 Hz) Adjustment of nugget: adjusted by welding current Ductility ratio: Cross tensile strength/Shea: tensile strength [0064] (Anti-delayed fraction property] After performing V-shaped bending using a 60° V-block of P. = 3 mm, stress of 1,500 MPa was applied to the bent portion, followed by immersion in an aqueous 5% hydrochloric acid solution. Then, the time until cracking occurs was measured.
The case where cracking did not occur after 48 hours was rated good anti-delayed fraction property (0) [0065]
Table 1
Chemical components (% by mass) St1typt C Si Mn P S Al Cr Nb Ti Others A) point A 0.17 1.7 2.3 0.010 0.002 0.045 ________ ________ 0.76 858 ________ 0.23 1.8 2.3 0.005 0.002 0.045 _____ Ca:0.002 0.80 846 C 0. 17 2.3 2 0.005 0.002 0.045 ________ 1.17 891 D 0.17 2.3 2.6 0.005 0.002 0. 045 ________ ________ 0.90 873 E 0.1.4 --2.0 2.5 0.005 0.002 0.045 -0.82 870 F 0.20 1.6 -2.04 0.005 0.002 0.045 *. 0.81 851 G 0.17 1.8 2.1 0.005 0.002 0045 0.2 -0.80 863 Ii 0.17 1.8 2.2 -. 0.001 0.002 0.045 0.04 0.84 859 T 0.17 1.8 2.3 0.001 0.002 0.045 _____ 0.05 0.80 856 J 0.16 1.8 2.4 0.010 0.001 0.15 -. 0.81 904 K 0.08 1.6 1.6 0.010 0.003 0.040 --1.03 899 L 0.22 0.5 2.8 0.010 0.003 0.040 0.5 _______ 0.19 -771 M 0.17 1.8 1.2 0.010 0. 003 0.040 -..----1.53 894 N 0.23 2.3 1.5 0.010 0.003 0.040 ________ 1.56 893 0 0.18 1.5 2.1 0.010 0.002 0.040 0.2 0.05 Ca:0.002 0.73 849 [0066]
Table 2
_____________ UeI. 1caLcnert condltjon T t N St Annealing Coinj rate Cooling rate CTemperatiire T2)Holdiiag T3 (Holding e.. . ce]. type tempereturu 1 2 at 1n1tiaton terrnj.jiutjon temperature: tureperature: (°C) (°c) (°c) cooiir1g rate _____________ Vrj: C) -1 A 900 -50 20 580 420 400 2 B --880 50 20 580 420 380 3 C 930 100 20 580 -420 380 4 -D 910 --50 20 -580 420 380 -5 E_____ 900 50 20 580 420 300 6 F 890 100 20 580 420 380 7 G 900 50 20 580 -420 -380 8 H 900 --50 20 580 420 360 9 I 900 50 20 560 420 360 J 940 50 20 580 420 380 -11 K 920 50 50 440 340 12 L 820 50 50 ----380 380 13 M 890 50 0 -380 380 14 920 -50 50 -400 360 A 820 30 20 600 360 360 16 --0 880 30 20 550 420 400 [0067]
Table 3
I Metj Lructura _________ Physical Propties Test 9teel Reaidual Art-de1ay . type PF BF 0arant grain yp RI ?. YR TSxEI TSx? Spotwe1da (U (9) (%) S1& (MPa) IMPa) 1%) (MPax%) (MPax%) (MPax%) bility property ___ (u) ___ A 18.2 12 69.3 < 1 s.5 650 9fl 21.2 41 0.66 20890 0309 -0 0 2 B 10. 13 76.7 < 1 3. 735 1097 21.3 44 0.67 23400 48619 0 0 3 C 28 56.5 < 1 8.7 647 1096 20.4 38 0.59 22350 1R00 0 0 4 0 9.1 14 76.4 3.3CM) 6.1 778 1235 19.2 43 0.63 23720 53025 0 0 E 22.7 -9 67.6 2.4(M) 7. 4 744 11.63 16.7 50 0.64 19430 58308 0 0 6 F 25.5 10 64. 1 8.6 643 1020 19. 9 46 0.63 19304 46737 0 0 7 5 17.3 12 70.2 < 1 6.1 651 1085 19.5 42 0.60 20120 46093 0 0 8 1 16.8 13 69.7 1 5.9 728 1056 19.4 48 0.69 20487 50299 0 0 9 -1 15.4 13 71.1 < 1 5.6 730 JOOS 19.7 48 (L68 20330 S1,io 0 0 J 20.1 12 67.4 2.5 8.4 746 111 17.6 50 0.67 19548 56055 0 -0 11 K 50.3 6 3. 7 1FJ(B+M) 0.7 516 836 21.4 34 0.62 17060 28595 0 12 L 11 -0 69 20(M,.B) 4. 1 703 1118 15.0 27 0.70 16740 29797 C) x 13 -M 72 14 13.5 9(M) 9.0 544 907 23.2 20 0.60 21013 18589 0 0 11 N 35 0 55 2 15.7 533 920 71.2 25 0.58 19532 23063 x 0 A 60 14 25.5 3.5(M) .9 676 1090 17.4 22 0.62 18012 23448 0 X 16 0 25 13 61.5 <1 3.5 680 1110 17.9 45 0.62 19912 50220 0 0 Note: PF: Polygonal ferrite, BF: Bairi.Ltic ferrite Remnant CM: Martensjte, B: Bainite) [0068J The following facts become apparent from the results shown in Tables 1 to 3.
[0069] Tests Nos. 1 to 10 and 16 are Exanpies which satisfy all defined features of the present invention. All steel materials have a tensile strength of 980 MPa or higher class and have good formability evaluated by strength x elongation characteristics and strength x stretch flangeability characteristics, and also have good soot-weldability and ant:-deayed fraction property.
[0070) In contrast, in Test No. 11, since the steel material has a low C content and also has a low bainitic ferrite content in the metal structure, it 1-ias poor tensile strength and also has poor formability evaluated by strength x elongation characteristics and strength x stretch flangeability characteristics. ifl Test No. 12, since the steel material has low Si content and also has a ratio (Si + Al)/(Mn + Cr) which is no: within a defined range, no residual? exist in the metal structure and aso has very poor formability evaluated by strength x elongation characteristics and strength x stretch flangeability characteristics, and poor anti-delayed fraction property.
[0071] Ir. Test No. 13, since the Mi content is not within a defined range and the ratio (Si + Al)/Mn exceeds a defined range, polygonal ferrite excessively increases and the amount of bainitic ferrite drastically decreases, and thus the steel material has low strength and very poor workability. In Test No. 14, although each content satisfies defined constituents, the ratio (Si + A1)/Mn exceeds a defined range and polygonal ferrite is coarse and an average grain size exceeds a defined value, and thus the steel material has low strength, poor workability and poor spot-weldab�lity.
[0072] In. Test No. 15, although the steel components satisfy defined constit',.ients, since the heat treatment conditions are not proper, the amount of polygonal ferrite in the structure excessively increases and the bainitic amount is low, and thus the steel material has very poor formability evaluated by strength x elongation characteristics and strength x stretch flangeability characteristics, and also has poor anti-delayed fraction property.
Claims (5)
1. A high-strength composite steel sheet having excellent formability and anti-delayed fraction property, comprising a steel satisfying: C: 0.10 to 0.25% (% by mass in case of a chemical component, the same shall apply hereinafter), Si: 1.0 to 3.0%, Mn: 1.5 to 3.0%, P: 0.15% or less, S: 0.02% or less, Al: 0.4% or less, and comprising the remnant made from iron and unavoidable impurities, wherein the contents of Si, Al and Mn satisfy the relationship of the following formula (I) (Si + A1)/Mn: 0.74 to 1.26 (I) and a microstructure in a longitudinal section comprisres, by an occupancy ratio based on the entire structure, 1) bainitic ferrite: 50% or more, 2) polygonal ferrite: 5 Lo 35%, 3) average grain size of polygonal ferrite: 1C p.m or less], and 4) residual austenite: 5% or more.
2. A high-strength comoosite steel sheet having excellent formability and anti-delayed fraction property, comprising a steel satisfying: C: 0.12 to 0.25%, Si: 1.0 to 3.0%, Mn: 1.5 to 3.0%, Cr: 1.0% or less, F: 0.15% or less, S: 0.02% or less, Al: 0.4% or less, and comprising the remnant made from iron and unavoidable impurities, wherein the contents of Si, Al, Mn and Cr satisfy the relationship of the following formula (II): (Si Al)/(Mn + Cr): 0.74 to 1.26 (II) and a microstructure in a longitudinal section comprises, by an occupancy ratio based on the entire structure, 1) bainitic ferrite: 50% or more, 2) polygonal ferrite: 5 to 35%, 3) average grain size of polygonal ferrite: 10 pm or less], and 4) residual austenite: 5% or more.
3. The high-strength composite steel sheet according to claim J. or 2, wherein zhe steel further contains, as other elements, Ti: 0.15% or less and/or Nb: 0.1% or less.
4. The high-strength composite steel sheet according to claim 1 or 2, wherein the steel further cor.tains, Ca: 30 ppm or less and/or REM: 30 ppm or less as other elements.
5. The high-strength composite steel sheet according to claim 1 or 2, which has a tensile strength of 980 MPa or higher.
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JP2005146301A (en) * | 2003-11-11 | 2005-06-09 | Kobe Steel Ltd | High-strength hot-rolled steel plate superior in formability |
JP2005220440A (en) * | 2004-01-09 | 2005-08-18 | Kobe Steel Ltd | Ultrahigh-strength steel sheet superior in hydrogen embrittlement resistance and manufacturing method therefor |
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EP3050988A4 (en) * | 2013-09-27 | 2017-03-08 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | High-strength steel sheet having excellent ductility and low-temperature toughness, and method for producing same |
US10066274B2 (en) | 2013-09-27 | 2018-09-04 | Kobe Steel, Ltd. | High-strength steel sheet having excellent ductility and low-temperature toughness, and method for producing same |
EP3235913A4 (en) * | 2014-12-19 | 2018-05-30 | Baoshan Iron & Steel Co., Ltd. | High-strength high-tenacity steel plate with tensile strength of 800 mpa and production method therefor |
Also Published As
Publication number | Publication date |
---|---|
GB0900057D0 (en) | 2009-02-11 |
JP4974341B2 (en) | 2012-07-11 |
JP2007321237A (en) | 2007-12-13 |
WO2007142197A1 (en) | 2007-12-13 |
CN101460646B (en) | 2012-10-10 |
US20100221138A1 (en) | 2010-09-02 |
GB2452230B (en) | 2012-02-22 |
CN101460646A (en) | 2009-06-17 |
KR20090016500A (en) | 2009-02-13 |
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