WO2016084847A1 - 高強度高延性鋼板 - Google Patents
高強度高延性鋼板 Download PDFInfo
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- WO2016084847A1 WO2016084847A1 PCT/JP2015/083078 JP2015083078W WO2016084847A1 WO 2016084847 A1 WO2016084847 A1 WO 2016084847A1 JP 2015083078 W JP2015083078 W JP 2015083078W WO 2016084847 A1 WO2016084847 A1 WO 2016084847A1
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Definitions
- the present invention relates to a high-strength, high-ductility steel sheet useful as an automatic thin steel sheet, and more particularly to a technique for improving the strength / ductility balance of a steel sheet.
- Patent Document 1 when the form of retained austenite in a steel structure is classified into a lath shape and an island shape, the ratio of the island-like retained austenite is controlled within a certain range, so that elongation and press forming stability are controlled.
- a high-strength thin steel sheet excellent in resistance has been proposed.
- good elongation at room temperature good elongation at a temperature of 100 to 200 ° C. has been realized, but YR, which is an effective material factor for impact characteristics, and a sufficient strength-ductility balance It is assumed that it has not been secured, and it is not considered to satisfy the above demand level.
- Patent Document 2 proposes a high-strength cold-rolled steel sheet that significantly improves the uniform elongation in the 45 ° direction relative to the rolling direction by increasing the degree of accumulation of the crystal orientation of the austenite phase in the steel structure. Yes.
- the characteristics in the rolling direction and the direction perpendicular to the rolling which are general ductility evaluation directions, are not specially mentioned and are not considered to satisfy the above-mentioned desired level.
- Patent Document 3 proposes a high-strength thin steel sheet that has improved paint bake hardenability and strength-ductility balance by imparting a C concentration difference between the surface and inside of retained austenite grains in the steel structure. Yes.
- the C concentration difference is imparted to the residual austenite grains only for the purpose of improving the baking bake hardenability, and as in the present invention, the stability of the residual austenite is improved. It is not intended to give the required carbon concentration distribution to the retained austenite in order to increase ductility, and is completely different from the technical idea of the present invention.
- an object of the present invention is to provide a strength-ductility balance that can ensure a yield ratio (YR) of 0.7 or more and tensile strength (TS) ⁇ elongation (EL ⁇ stretch flangeability ( ⁇ ) of 1000000 MPa ⁇ % ⁇ % or more.
- An object of the present invention is to provide a high-strength and high-ductility steel sheet that is excellent in the above.
- the high strength and high ductility steel sheet according to the first invention of the present invention is Ingredient composition is mass%, C: 0.10% or more, less than 0.35%, Si + Al: 0.5 to 2.0%, Mn: 1.0 to 4.0%, P: 0 to 0.05% S: 0 to 0.01%
- the balance consists of iron and inevitable impurities, Steel structure Residual austenite is 8% or more in area ratio to the whole structure And the balance consists of one or more of bainite, martensite, tempered bainite, and tempered martensite, Regarding the carbon concentration in the retained austenite, Its average carbon concentration is 0.9-1.2% by mass, The standard deviation of the carbon concentration distribution is 0.35% by mass or more, The area
- the high strength and high ductility steel sheet according to the second invention of the present invention is in the first invention, Ingredient composition is mass%, and One or two or more of Cu, Ni, Mo, Cr and B are contained in total of 1.0% or less.
- the high strength and high ductility steel sheet according to the third aspect of the present invention is in the first or second invention, Ingredient composition is mass%, and One or more of V, Nb, Ti, Zr and Hf are contained in a total of 0.2% or less.
- the high strength and high ductility steel sheet according to the fourth aspect of the present invention is in any one of the first to third inventions, Ingredient composition is mass%, and One or two or more of Ca, Mg, and REM are included in a total of 0.01% or less.
- the TRIP phenomenon can be developed from the early stage to the late stage of deformation.
- the yield ratio (YR) is 0.7 or more, and the tensile strength (TS) ⁇ elongation (EL) ⁇ stretch flangeability ( ⁇ ) can be ensured to be 1000000 MPa ⁇ % ⁇ % or more. It has become possible to provide a high-strength, high-ductility steel sheet with an excellent balance between strength and ductility.
- the present inventors have obtained a steel sheet made of TBF steel as its mechanical properties with a yield ratio (YR) of 0.7 or more, tensile strength (TS) ⁇ elongation (EL) ⁇ elongation.
- YR yield ratio
- TS tensile strength
- EL elongation
- ⁇ flangeability
- residual ⁇ retained austenite
- the present inventors paid attention to the carbon concentration distribution in the residual ⁇ . That is, in order to achieve high strength and high ductility by the TRIP phenomenon, it is important to achieve a high work hardening rate from the initial stage to the middle stage of deformation, and for this purpose, unstable residual ⁇ with a low carbon concentration. There must be some. On the other hand, in order to maintain a high work hardening rate even when the amount of deformation increases, that is, in the later stage of deformation, it is necessary to create a stable residual ⁇ having a high carbon concentration.
- the residual ⁇ is not only high stability or low stability alone, and that there is a wide range of stability, that is, carbon concentration distribution.
- structure that characterizes the high-strength and high-ductility steel sheet (hereinafter also referred to as “the steel sheet of the present invention”) according to the present invention will be described.
- the steel sheet of the present invention is based on the structure of TBF steel.
- the carbon concentration distribution in the residual ⁇ is controlled. This is different from the prior art.
- Residual austenite 8% or more in area ratio with respect to the whole structure> Residual ⁇ is useful for improving ductility, and in order to exert such an effect effectively, the area ratio to the whole tissue should be 8% or more, preferably 9% or more, more preferably 10% or more. is necessary.
- the area ratio of residual ⁇ is preferably 20% or less, more preferably 18% or less, and particularly preferably 16% or less.
- ⁇ Balance one or more of bainite, martensite, tempered bainite, and tempered martensite>
- % C ⁇ R ⁇ Average carbon concentration in residual ⁇ (% C ⁇ R ): 0.9 to 1.2% by mass> % C ⁇ R is an index that affects the stability with which residual ⁇ transforms into martensite during deformation. If% C ⁇ R is too low, the residual ⁇ is unstable, and after the application of stress, the work-induced martensitic transformation occurs before plastic deformation, and the required elongation cannot be obtained. On the other hand, if% C ⁇ R is too high, the residual ⁇ becomes too stable, and even if processing is applied, the processing-induced martensitic transformation does not occur, so that the required stretch flangeability cannot be obtained. In order to obtain the required elongation,% C ⁇ R needs to be 0.9 to 1.2% by mass. A preferable lower limit of% C ⁇ R is 1.0% by mass.
- ⁇ Standard deviation of carbon concentration distribution in residual ⁇ 0.35 mass% or more> This is because, in order to increase and maintain the work hardening rate from the initial stage to the late stage of the deformation, the residual ⁇ having different stability is created by widening the carbon concentration distribution in the residual ⁇ .
- the standard deviation of the carbon concentration distribution in the residual ⁇ is 0.35% by mass or more, preferably 0.40% by mass or more, more preferably 0.45% by mass or more.
- the upper limit of the standard deviation of the carbon concentration distribution in the residual ⁇ is practically about 0.70% by mass, preferably 0.65% by mass or less.
- the area where the carbon concentration in the residual ⁇ is 1.5% by mass or more is 1.0% or more, preferably 1.5% or more, more preferably 2.0% or more in terms of the area ratio to the whole structure It is necessary to let In the high-strength and highly ductile steel sheet according to the present invention, the area ratio of the carbon concentration in the residual ⁇ of 1.5% by mass or more with respect to the entire structure has an upper limit of about 1/2 of the total residual ⁇ area. , Preferably 2/5 or less, more preferably 1/3 or less.
- the area ratio (V ⁇ R ) and average carbon concentration (% C ⁇ R ) of residual ⁇ were measured by X-ray diffraction after grinding to a thickness of 1 ⁇ 4 of the steel sheet and then chemical polishing (ISIJ Int. Vol. 33, (1933), No. 7, p. 776).
- a two-dimensional micro part X-ray diffractometer (RINT-RAPIDII) manufactured by Rigaku Co., Ltd. was used as the X-ray diffractometer, and a Co—K ⁇ ray was used as the X-ray.
- the steel sheet was subjected to nital corrosion and observed with an optical microscope (magnification 400 times) to identify a structure other than the residual ⁇ .
- % C avg (1 / 0.033) ⁇ (a 0 ⁇ 0.0012 ⁇ % Mn + 0.00157 ⁇ % Si ⁇ 0.0056 ⁇ % Al)
- % Mn,% Si, and% Al are the contents (mass%) of Mn, Si, and Al, respectively, in the steel sheet.
- the diffraction angles at the upper and lower limits of the half width ⁇ 2 ⁇ (hkl) of the diffraction angle 2 ⁇ (hkl) of each peak were determined by the following formulas (4) and (5) (see FIG. 1).
- the standard deviation ⁇ % C was calculated from the half-value width ⁇ % C as follows.
- the probability density function f (x) of the normal distribution is expressed by the following formula (7) from the average value u and the standard deviation ⁇ .
- equation (9) is obtained from equations (7) and (8). The relationship is obtained.
- ⁇ % C ⁇ ⁇ ( ⁇ % C / 2) 2 / (2ln2) ⁇ (10)
- the carbon concentration is 1 by the cumulative density function g (x) shown in the following formula (11). .5% by weight or more areas, to derive the following equation (12) as an expression for obtaining the area ratio V [gamma] R (C ⁇ 1.5%) for all tissues, V [gamma] R (C ⁇ using this equation (12) 1.5%) was calculated.
- V ⁇ R is the area ratio of the total residual ⁇ .
- Component composition of the steel sheet of the present invention C: 0.10% or more and less than 0.35% C contributes to securing the amount (area ratio) of retained austenite and is an essential element for securing strength and ductility. In order to effectively exhibit such an action, it is necessary to contain C by 0.10% or more, preferably 0.12% or more, more preferably 0.14% or more. However, since the weldability is deteriorated when the C amount becomes excessive, the C amount is less than 0.35%, preferably 0.32% or less, more preferably 0.30% or less, and further preferably 0.28% or less. And
- Si and Al are elements that effectively suppress the decomposition of residual austenite and the formation of carbides. In order to effectively exhibit such an action, it is necessary to contain Si and Al in total of 0.5% or more, preferably 0.7% or more, and more preferably 0.9% or more. However, even if Si and Al are contained excessively, the above effect is saturated and not only is economically wasteful but also causes hot brittleness, so the total amount of Sl and Al is 2.0% or less. 1.9% or less, more preferably 1.8% or less.
- Mn 1.0 to 4.0% Mn is an element necessary for stabilizing austenite and obtaining desired retained austenite. In order to effectively exhibit such an action, it is necessary to contain Mn at 1.0% or more, preferably 1.3% or more, more preferably 1.6% or more. However, if the amount of Mn is excessive, adverse effects such as occurrence of cracking of the cast slab are observed, so the amount of Mn is 4.0% or less, preferably 3.5% or less, more preferably 3.0% or less.
- P 0 to 0.05% P inevitably exists as an impurity element, but is an element that may be contained in order to ensure a desired residual ⁇ . However, if P is excessively contained, secondary workability deteriorates, so the amount of P is 0.05% or less, preferably 0.03% or less, and more preferably 0.02% or less.
- S 0 to 0.01% Since S is also unavoidably present as an impurity element and forms sulfide-based inclusions such as MnS and becomes a starting point of cracking and deteriorates workability, the amount of S is 0.01% or less, preferably 0.005% or less, more preferably 0.003% or less.
- the steel of the present invention contains the above-described elements as essential components, and the balance is iron and inevitable impurities.
- the following allowable components can be contained within the range not impairing the action of the present invention.
- One or more of Cu, Ni, Mo, Cr, and B are useful as steel strengthening elements, as well as for stabilizing residual ⁇ and securing a predetermined amount. It is an effective element. In order to effectively exhibit such an action, it is recommended that these elements are contained in a total amount of 0.001% or more, and further 0.01% or more. However, even if these elements are contained excessively, the above effect is saturated and is economically wasteful. Therefore, these elements are added in a total amount of 1.0% or less, and further 0.5% or less. Is preferred.
- V, Nb, Ti, Zr, and Hf 0.2% or less in total
- These elements have the effect of precipitation strengthening and refinement of the structure, and are useful elements for increasing the strength. In order to effectively exhibit such an action, it is recommended that these elements are contained in a total amount of 0.01% or more, and further 0.02% or more. However, even if these elements are contained excessively, the above effects are saturated and economically useless. Therefore, these elements are 0.2% or less in total amount, and further 0.1% or less. It is preferable to do this.
- One or more of Ca, Mg and REM 0.01% or less in total
- These elements are elements that control the form of sulfides in steel and are effective in improving workability.
- examples of the REM (rare earth element) used in the present invention include Sc, Y, and lanthanoid.
- these elements are 0.01% or less in total amount, further 0.005% or less. It is preferable to do this.
- the steel sheet of the present invention can be produced by hot-rolling a steel material satisfying the above component composition, followed by cold rolling, and then performing a heat treatment, for example, under the conditions of the following steps (1) to (4). (See FIG. 2).
- the holding time t2 in the temperature range is more preferably 10 s or more, and further preferably 20 s or more, but it is recommended that the holding time t2 be 200 s or less from the viewpoint of productivity.
- Ac1 and Ac3 are derived from the chemical composition of the steel sheet, by Lesley, “Iron & Steel Materials Science”, translated by Koda Narumi, Maruzen Co., Ltd., 1985, p. 273 can be obtained using the equation described in H.273.
- Third heating holding temperature T3 [Ac3 + 10 ° C.] to 950 ° C.
- Third holding time t3 holding 180 s or less> This is to prevent the ferrite from remaining until the subsequent cooling by making the structure into an austenite single phase structure by holding in the austenite single phase region temperature region. If the third heating temperature T3 is less than [Ac3 + 10 ° C.], ferrite remains, and ferrite growth cannot be suppressed in the subsequent cooling process of the above step (3), and ferrite is excessively formed. On the other hand, when the third heating temperature T3 exceeds 950 ° C. or the third holding time t3 exceeds 180 s, Mn distributed during the two-phase heating in the step (1) becomes uniform, and the residual ⁇ The carbon concentration distribution cannot be widened.
- the average cooling rate HR3 in this temperature range is more preferably 25 ° C./s or more, and further preferably 30 ° C./s or more.
- Austempering temperature T4 350 to 480 ° C.
- austempering holding time t4 Hold for 10 s or more, then cool to room temperature> This is because bainite transformation is promoted and carbon is concentrated to untransformed austenite to obtain stable residual ⁇ .
- the cold-rolled sheet is heated to the first heating temperature T1: [Ac1-100 ° C.] to [Ac1-30 ° C.] and held at that temperature for the first holding time: 10 s or more, or within the same temperature range.
- the second heating temperature T2 [0.7 ⁇ Ac1 + 0.3 ⁇ Ac3] to [0.2 ⁇ Ac1 + 0.8 ⁇ Ac3] and the second holding time t2: Hold for 5 s or longer.
- Mn is concentrated in cementite by holding or gradually heating in the ferrite / cementite two-phase region temperature range for a predetermined time in advance, and between ferrite / austenite during the subsequent ferrite / austenite two-phase region heating.
- the local speed difference of the bainite transformation during the austempering treatment in the step (4) can be increased, and the carbon concentration distribution in the residual ⁇ can be broadened.
- step (4) may be configured as the following step (4a).
- Austempering temperature T4 Austempering holding time t4: held at 350 to 480 ° C. for 10 s or more
- reheating temperature T5 Reheated to 500 to 600 ° C.
- reheating holding time t5 30 s or less Cool to room temperature.
- the steel sheet of the present invention can be made into a plated steel sheet by reheating to a temperature range where the residual ⁇ does not decompose and alloying the plating layer.
- the steel plate of 30 mm in thickness After manufacturing the steel of the component shown in the following Table 1 by vacuum melting, it made the steel plate of 30 mm in thickness by hot forging, and then hot rolled.
- the hot rolling conditions do not substantially affect the final structure and properties of the steel sheet of the present invention, but in this example, after heating to 1200 ° C, the end temperature of hot rolling is 880 ° C in multi-stage rolling.
- the plate thickness was 2.5 mm under the conditions. Then, it cooled to 500 degreeC with the cooling rate of 30 degrees C / s, and stopped cooling, and after inserting in the furnace heated to 500 degreeC, it hold
- the hot-rolled sheet was pickled to remove the surface scale, and then cold-rolled to 1.4 mm to obtain a cold-rolled sheet.
- the average heating rate from room temperature to the first heating temperature (holding temperature) is constant 10 ° C./s
- the average heating rate from the next heating temperature (holding temperature) to 20 ° C./s is constant
- the next heating temperature The average heating rate up to (holding temperature) was fixed at 10 ° C./s.
- the average heating rate from the austempering temperature T4 to the reheating temperature T5 was constant 10 ° C./s
- the average cooling rate from the austempering temperature T4 or the reheating temperature T5 to room temperature was constant 10 ° C./s.
- the area ratio of residual ⁇ , the average carbon concentration (C ⁇ R) in the residual ⁇ , and the carbon concentration distribution thereof were determined by the measurement method described in the above section [Mode for Carrying Out the Invention]. It was measured.
- all the structures of the steel plates used in this example, the remainder other than retained austenite and ferrite were composed of one or more of bainite, martensite, tempered bainite, and tempered martensite. In Table 3, only the area ratios of retained austenite and ferrite are shown.
- the yield strength YS, tensile strength TS, and elongation (total elongation) EL were measured by a tensile test.
- the tension test produced the JIS No. 5 test piece and implemented according to JISZ2241.
- the hole expansion ratio was measured according to the Japan Iron and Steel Federation standard JFST1001.
- the properties of the steel sheet after the heat treatment are those with a yield ratio (YR) of 0.7 or more and tensile strength (TS) ⁇ elongation (EL) ⁇ stretch flangeability ( ⁇ ) of 1000000 MPa ⁇ % ⁇ % or more. Was determined to be acceptable (O), and the others were determined to be unacceptable (X).
- 3, 4, 9 to 11, 14, and 18 to 27 are invention steels that satisfy the requirements of the structure provision of the present invention as a result of heat treatment under the recommended conditions using steel types that satisfy the requirements of the composition provision of the present invention.
- a high-strength and ductile steel sheet having excellent mechanical properties satisfying the acceptance criteria and having an excellent balance between strength and ductility was obtained.
- steel No. which is a comparative steel (evaluation of x).
- Nos. 1, 2, 5 to 8, 12, 13, and 15 to 17 do not satisfy at least one of the component definition and the structure definition of the present invention, and the characteristics do not satisfy the acceptance criteria.
- Steel No. 1, 2, 5-8, and 12 use steel grades that satisfy the requirements of the component specifications of the present invention, but are manufactured under conditions that deviate from the recommended manufacturing conditions, so the requirements of the organization regulations are satisfied. The characteristics are inferior.
- steel No. 13 and 15 to 17 are manufactured under the recommended manufacturing conditions, steel grades that partially deviate from the requirements of the component provision of the present invention are used, so the requirements of the organization provision are not satisfied and the characteristics are inferior. .
- the steel sheet of the present invention is excellent in strength and ductility balance and is useful for automobile thin steel sheets and the like.
Abstract
Description
成分組成が、質量%で、
C:0.10%以上、0.35%未満、
Si+Al:0.5~2.0%、
Mn:1.0~4.0%、
P:0~0.05%、
S:0~0.01%
であり、残部が鉄および不可避的不純物からなり、
鋼組織が、
残留オーステナイトが全組織に対する面積率で8%以上
であり、残部がベイナイト、マルテンサイト、焼戻しベイナイト、および焼戻しマルテンサイトの1種または2種以上からなるとともに、
前記残留オーステナイト中の炭素濃度に関し、
その平均炭素濃度が0.9~1.2質量%、
その炭素濃度分布の標準偏差が0.35質量%以上、
その炭素濃度が1.5質量%以上の領域が全組織に対する面積率で1.0%以上であることを特徴とする。
上記第1発明において、
成分組成が、質量%で、さらに、
Cu、Ni、Mo、CrおよびBの1種または2種以上を合計で1.0%以下含むものである。
上記第1または第2発明において、
成分組成が、質量%で、さらに、
V、Nb、Ti、ZrおよびHfの1種または2種以上を合計で0.2%以下含むものである。
上記第1~第3発明のいずれか1つの発明において、
成分組成が、質量%で、さらに、
Ca、MgおよびREMの1種または2種以上を合計で0.01%以下含むものである。
上述したとおり、本発明鋼板は、TBF鋼の組織をベースとするものであるが、特に、所定の炭素濃度の残留γを所定量含有したうえで、その残留γ中の炭素濃度分布が制御されている点で、上記従来技術と相違している。
残留γは延性の向上に有用であり、このような作用を有効に発揮させるためには、全組織に対する面積率で8%以上、好ましくは9%以上、さらに好ましくは10%以上存在させることが必要である。なお、残留γの面積率は20%以下が好ましく、さらに好ましくは18%以下、特に好ましくは16%以下である。
フェライトの生成を防止し、微細で均一な組織であるベイナイトやマルテンサイト、および/またはそれらの焼戻し組織で母相を構築することで、母相組織の微細化によって、低荷重時における変形防止による降伏強度YSの上昇が可能となる。
%CγRは、変形時に残留γがマルテンサイトに変態する安定度に影響する指標である。%CγRが低すぎると、残留γが不安定なため、応力付与後、塑性変形する前に加工誘起マルテンサイト変態が起るため、所要の伸びが得られなくなる。一方、%CγRが高すぎると、残留γが安定になりすぎて、加工を加えても加工誘起マルテンサイト変態が起らないため、やはり所要の伸びフランジ性が得られなくなる。所要の伸びを得るためには、%CγRは0.9~1.2質量%とする必要がある。%CγRの好ましい下限は1.0質量%である。
変形の初期から後期にかけて加工硬化率を高め維持するために、残留γ中の炭素濃度分布を広げることで、安定性の異なる残留γを作り込むためである。このような作用を有効に発揮させるためには、残留γ中の炭素濃度分布の標準偏差は0.35質量%以上、好ましくは0.40質量%以上、さらに好ましくは0.45質量%以上とする必要がある。なお、本発明に係る高強度高延性鋼板においては、残留γ中の炭素濃度分布の標準偏差は実際上、0.70質量%程度が上限であり、好ましくは0.65質量%以下である。
伸びを高めるためには、ひずみ量が増加した際における、残留γの安定度が高いことが重要であり、そのためには、平均的に炭素濃度が高いだけでは十分でなく、安定度の高い、すなわち炭素濃度の高い残留γが一定量以上存在することが必要である。具体的には、残留γ中の炭素濃度が1.5質量%以上の領域が全組織に対する面積率で1.0%以上、好ましくは1.5%以上、さらに好ましくは2.0%以上存在させる必要がある。なお、本発明に係る高強度高延性鋼板においては、残留γ中の炭素濃度が1.5質量%以上の領域が全組織に対する面積率は、全残留γ面積の1/2程度が上限であり、好ましくは2/5以下、さらに好ましくは1/3以下である。
ここで、残留γの面積率、平均炭素濃度(%CγR)および炭素濃度分布の各測定方法について説明する。
ここに、%Mn、%Si、%Alは、それぞれ、鋼板中のMn、Si、Alの含有量(質量%)である。
2θH(hkl)=2θavg(hkl)+Δ2θ(hkl)/2・・・式(5)
=VγR[0.5-erf{(1.5-%Cavg)/√(2σ%C 2)}]・・・式(12)
ここに、VγRは全残留γの面積率である。
C:0.10%以上、0.35%未満
Cは、残留オーステナイトの量(面積率)の確保に寄与することで、強度と延性を確保するために必須の元素である。このような作用を有効に発揮させるためには、Cを0.10%以上、好ましくは0.12%以上、さらに好ましくは0.14%以上含有させる必要がある。ただし、C量が過剰になると、溶接性を劣化させるので、C量は0.35%未満、好ましくは0.32%以下、より好ましくは0.30%以下、更に好ましくは0.28%以下とする。
SiおよびAlは、残留オーステナイトが分解して炭化物が生成するのを有効に抑制する元素である。このような作用を有効に発揮させるためには、SiおよびAlを合計で0.5%以上、好ましくは0.7%以上、さらに好ましくは0.9%以上含有させる必要がある。ただし、SiおよびAlを過剰に含有させても、上記効果が飽和してしまい、経済的に無駄であるばかりでなく、熱間脆性を引き起こすため、SlおよびAlの合計量は2.0%以下、好ましくは1.9%以下、さらに好ましくは1.8%以下とする。
Mnは、オーステナイトを安定化し、所望の残留オーステナイトを得るために必要な元素である。このような作用を有効に発揮させるためには、Mnを1.0 % 以上、好ましくは1.3%以上、さらに好ましくは1.6%以上含有させることが必要である。ただし、Mn量が過剰になると、鋳片割れが生じる等の悪影響が見られるので、Mn量は4.0%以下、好ましくは3.5 %以下、さらに好ましくは3.0 %以下とする。
Pは不純物元素として不可避的に存在するが、所望の残留γを確保するために含有させてもよい元素である。ただし、Pを過剰に含有させると二次加工性が劣化するので、P量は0.05%以下、好ましくは0.03%以下、さらに好ましくは0.02%以下とする。
Sも不純物元素として不可避的に存在し、MnS等の硫化物系介在物を形成し、割れの起点となって加工性を劣化させる元素であるので、S量は0.01%以下、好ましくは0.005%以下、さらに好ましくは0.003%以下とする。
これらの元素は、鋼の強化元素として有用であるとともに、残留γの安定化や所定量の確保に有効な元素である。このような作用を有効に発揮させるためには、これらの元素は合計量で0.001%以上、さらには0.01%以上含有させることが推奨される。ただし、これらの元素を過剰に含有させても上記効果が飽和してしまい、経済的に無駄であるので、これらの元素は合計量で1.0%以下、さらには0.5%以下とするのが好ましい。
これらの元素は、析出強化および組織微細化の効果があり、高強度化に有用な元素である。このような作用を有効に発揮させるためには、これらの元素を合計量で0.01%以上、さらには0.02%以上含有させることが推奨される。ただし、これらの元素を過剰に含有させても、上記効果が飽和してしまい、経済的に無駄であるので、これらの元素は合計量で0.2%以下、さらには0.1%以下とするのが好ましい。
これらの元素は、鋼中硫化物の形態を制御し、加工性向上に有効な元素である。ここで、本発明に用いられるREM(希土類元素)としては、Sc、Y、ランタノイド等が挙げられる。上記作用を有効に発揮させるためには、これらの元素を合計量で0.001%以上、さらには0.002%以上含有させることが推奨される。ただし、これらの元素を過剰に含有させても、上記効果が飽和してしまい、経済的に無駄であるので、これらの元素は合計量で0.01%以下、さらには0.005%以下とするのが好ましい。
本発明鋼板は、上記成分組成を満足する鋼材を、熱間圧延し、ついで冷間圧延した後、例えば下記の工程(1)~(4)の条件にて熱処理を行って製造することができる(図2参照)。
(1)冷延板を第2加熱温度T2:[0.7×Ac1+0.3×Ac3]~[0.2×Ac1+0.8×Ac3]に加熱してその温度で第2保持時間t2:5s以上保持するか、または、同温度範囲を4℃/s以下の平均加熱速度で加熱した後、
(2)さらに第3加熱温度T3:[Ac3+10℃]~950℃に加熱し、その温度で第3保持時間t3:180s以下保持したのち、
(3)上記第3加熱温度T3から500℃までを平均冷却速度CR1:20℃/s以上で冷却した後、
(4)オーステンパ温度T4:350~480℃でオーステンパ保持時間t4:10s以上保持後、室温まで冷却する。
フェライト/オーステナイトの2相域温度領域にて所定時間保持または徐加熱することで、この2相域温度領域にて逆変態中にMn濃度分配を起こさせることにより、上記工程(4)におけるオーステンパ処理時のベイナイト変態の局所的な速度差を大きくし、残留γ中の炭素濃度分布を広くするためである。
当該温度範囲における保持時間t2は、より好ましくは10s以上、さらに好ましくは20s以上であるが、生産性の観点から200s以下とすることが推奨される。
なお、Ac1およびAc3は、鋼板の化学成分から、レスリー著、「鉄鋼材料科学」、幸田成靖 訳、丸善株式会社、1985年、p.273に記載の式を用いて求めることができる。
オーステナイト単相域温度領域にて保持することで、組織をオーステナイト単相組織とすることにより、その後の冷却時にまでフェライトが残存することを防止するためである。
第3加熱温度T3を[Ac3+10℃]未満とすると、フェライトが残存し、その後の上記工程(3)の冷却過程でフェライトの成長を抑制できず、フェライトが過剰に形成される。一方、第3加熱温度T3を950℃超、または、第3保持時間t3を180s超とすると、上記工程(1)にて2相域加熱時に分布したMnが均一化してしまい、残留γ中の炭素濃度分布を広くできなくなる。
フェライトの形成を防止し、ベイナイト主体の組織にするためである。
この温度範囲における平均冷却速度HR3は、より好ましくは25℃/s以上、さらに好ましくは30℃/s以上である。
ベイナイト変態を促進させて、未変態オーステナイトへ炭素を濃化させることで、安定な残留γを得るためである。
なお、上記工程(1)は、下記工程(1a)のように構成してもよい。
なお、本実施例において使用した鋼板の組織は全て、残留オーステナイトおよびフェライト以外の残部はベイナイト、マルテンサイト、焼戻しベイナイト、および焼戻しマルテンサイトの1種または2種以上からなるものであったので、下記表3にては、残留オーステナイトおよびフェライトの面積率のみを記載した。
本出願は、2014年11月26日出願の日本特許出願(特願2014-238710)に基づくものであり、その内容はここに参照として取り込まれる。
Claims (2)
- 成分組成が、質量%で、
C:0.10%以上、0.35%未満、
Si+Al:0.5~2.0%、
Mn:1.0~4.0%、
P:0~0.05%、
S:0~0.01%
であり、残部が鉄および不可避的不純物からなり、
鋼組織が、
残留オーステナイトが全組織に対する面積率で8%以上であり、残部がベイナイト、マルテンサイト、焼戻しベイナイト、および焼戻しマルテンサイトの1種または2種以上からなるとともに、
前記残留オーステナイト中の炭素濃度に関し、
その平均炭素濃度が0.9~1.2質量%、
その炭素濃度分布の標準偏差が0.35質量%以上、
その炭素濃度が1.5質量%以上の領域が全組織に対する面積率で1.0%以上
であることを特徴とする高強度高延性鋼板。 - 成分組成が、質量%で、さらに 下記(a)~(c)の何れか1つを含むものである請求項1記載の高強度高延性鋼板。
(a)Cu、Ni、Mo、CrおよびBの1種または2種以上を合計で1.0%以下
(b)V、Nb、Ti、ZrおよびHfの1種または2種以上を合計で0.2%以下
(c)Ca、MgおよびREMの1種または2種以上を合計で0.01%以下
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US (1) | US20170268077A1 (ja) |
EP (1) | EP3225708A4 (ja) |
JP (1) | JP6282577B2 (ja) |
KR (1) | KR102111921B1 (ja) |
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Cited By (3)
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JP2019534941A (ja) * | 2016-10-31 | 2019-12-05 | バオシャン アイアン アンド スティール カンパニー リミテッド | 引張強度が1500MPa以上で、かつ成形性に優れた冷間圧延高強度鋼及びその製造方法 |
WO2020148948A1 (ja) * | 2019-01-18 | 2020-07-23 | Jfeスチール株式会社 | 高強度溶融亜鉛めっき鋼板およびその製造方法 |
CN113308593A (zh) * | 2021-05-28 | 2021-08-27 | 四川大学 | 一种基于碳配分和两步等温淬火的中碳硅锰低合金钢热处理工艺 |
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WO2017208763A1 (ja) * | 2016-05-30 | 2017-12-07 | 株式会社神戸製鋼所 | 高強度鋼板およびその製造方法 |
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WO2018115936A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | Tempered and coated steel sheet having excellent formability and a method of manufacturing the same |
JP6860420B2 (ja) * | 2017-05-24 | 2021-04-14 | 株式会社神戸製鋼所 | 高強度鋼板およびその製造方法 |
JP6849536B2 (ja) * | 2017-05-31 | 2021-03-24 | 株式会社神戸製鋼所 | 高強度鋼板およびその製造方法 |
EP3688203B1 (de) * | 2017-09-28 | 2022-04-27 | ThyssenKrupp Steel Europe AG | Stahlflachprodukt und verfahren zu seiner herstellung |
EP4079943A4 (en) * | 2019-12-20 | 2022-12-21 | Nippon Steel Corporation | NICKEL-PLATED STEEL SHEET AND METHOD OF PRODUCTION OF NICKEL-PLATED STEEL SHEET |
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- 2015-11-25 US US15/528,675 patent/US20170268077A1/en not_active Abandoned
- 2015-11-25 WO PCT/JP2015/083078 patent/WO2016084847A1/ja active Application Filing
- 2015-11-25 KR KR1020177013590A patent/KR102111921B1/ko active IP Right Grant
- 2015-11-25 EP EP15862199.5A patent/EP3225708A4/en not_active Withdrawn
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JP2019534941A (ja) * | 2016-10-31 | 2019-12-05 | バオシャン アイアン アンド スティール カンパニー リミテッド | 引張強度が1500MPa以上で、かつ成形性に優れた冷間圧延高強度鋼及びその製造方法 |
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Also Published As
Publication number | Publication date |
---|---|
CN107002192B (zh) | 2019-03-08 |
EP3225708A1 (en) | 2017-10-04 |
CN107002192A (zh) | 2017-08-01 |
EP3225708A4 (en) | 2018-05-02 |
JP6282577B2 (ja) | 2018-02-21 |
JP2016098427A (ja) | 2016-05-30 |
KR20170070230A (ko) | 2017-06-21 |
KR102111921B1 (ko) | 2020-05-18 |
US20170268077A1 (en) | 2017-09-21 |
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