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WO2017149999A1 - Tôle d'acier destinée à être durcie, élément durci et procédé de fabrication de tôle d'acier destinée à être durcie - Google Patents

Tôle d'acier destinée à être durcie, élément durci et procédé de fabrication de tôle d'acier destinée à être durcie Download PDF

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Publication number
WO2017149999A1
WO2017149999A1 PCT/JP2017/002186 JP2017002186W WO2017149999A1 WO 2017149999 A1 WO2017149999 A1 WO 2017149999A1 JP 2017002186 W JP2017002186 W JP 2017002186W WO 2017149999 A1 WO2017149999 A1 WO 2017149999A1
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steel sheet
quenching
temperature
concentration
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PCT/JP2017/002186
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English (en)
Japanese (ja)
Inventor
紗江 濱本
達也 浅井
裕之 大森
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Kobe Steel Ltd
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Kobe Steel Ltd
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Publication date
Priority claimed from JP2016207673A external-priority patent/JP2017155329A/ja
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Priority to CN201780013823.XA priority Critical patent/CN108779527A/zh
Priority to MX2018010347A priority patent/MX2018010347A/es
Priority to BR112018067894A priority patent/BR112018067894A2/pt
Priority to CA3015966A priority patent/CA3015966A1/fr
Priority to US16/080,566 priority patent/US20190017142A1/en
Priority to EP17759471.0A priority patent/EP3421631A4/fr
Priority to KR1020187026939A priority patent/KR20180117127A/ko
Publication of WO2017149999A1 publication Critical patent/WO2017149999A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/18—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

Definitions

  • the present invention relates to a steel plate for quenching, a quenching member, and a method for producing a steel plate for quenching. More specifically, a steel sheet for quenching useful as a material for providing a quenching member having excellent bending workability in T-direction bending in which the bending ridge line is parallel to the rolling direction in a region where the hardness after quenching is 515 HV or more. And a manufacturing method thereof.
  • a hot press forming technique is adopted in which press forming is performed with a mold in a state where the strength is lowered by heating to a temperature at which the austenite single phase is formed, and the forming is facilitated.
  • the tensile strength of the hot press-formed product is increased, breakage tends to occur at the time of collision.
  • the bendability of the hot press-formed product needs to be excellent.
  • Examples of the steel material for hot press working used for hot press-molded products include steel materials described in Patent Document 1 and Patent Document 2.
  • Patent Document 1 describes a steel material for hot press working that has a specific chemical composition and has a steel structure in which the spheroidization rate of carbides in steel is 0.60 to 0.90.
  • Patent Document 2 has a specific chemical composition, a steel structure having a prior austenite average particle size of 10 ⁇ m or less, and mechanical properties having a tensile strength of 1.8 GPa or more and 2.0 GPa or less. A hot pressed steel sheet member is described.
  • the present invention provides a quenched member excellent in T-direction bendability, a quenched steel plate capable of producing the quenched member, and a method for producing the same, even in a high-strength region having a hardness after quenching of 515 HV or higher. With the goal.
  • the component composition is mass%, C: more than 0.2% and 0.4% or less, Si: 0.8% or more and 1.4% or less, Mn: 1% or more and 3% or less, P: more than 0% and 0.02% or less, S: more than 0% and 0.002% or less, sol.
  • [Mn] Mn concentration (% by mass) of the steel sheet analyzed by inductively coupled plasma emission spectroscopy
  • S1 Area% of the region where the Mn concentration analyzed by the electron microprobe analyzer is more than twice the above [Mn] in the structure of the steel plate at the thickness 1/4 position.
  • S2 Area% of a region in which the Mn concentration analyzed by an electron beam microprobe analyzer is 0.5 times or less of the above [Mn] in the structure of the steel plate with a thickness of 1/4.
  • FIG. 1 is a diagram showing the relationship between the hardness of the quenched member and the T-direction bending angle.
  • the steel sheets described in Patent Document 1 and Patent Document 2 have excellent bending workability in L-direction bending in which the bending ridge line is perpendicular to the rolling direction, but the bending ridge line It has been found that the bending workability of T-direction bending (hereinafter referred to as T-direction bending property) that is parallel to the rolling direction is insufficient.
  • the hot press forming technique has been described as an example.
  • the above problem that it is difficult to achieve both high strength and bendability is a hot press. It is not limited to molded products but can be found in all hardened members.
  • the present inventors provide a steel sheet for quenching that can be a quenching member excellent in T-direction bendability even when the tensile strength after quenching is about 1600 MPa or higher, that is, the hardness after quenching is high strength of 515 HV or higher. For this reason, we have been studying earnestly.
  • quenching means not only a mode in which a press working is performed in a softened state by heating to about 900 ° C. as in a hot press, and at the same time quenching is performed by a cooling effect accompanying contact with a mold. It is also intended to include a mode in which quenching is performed after press working such as warm press and cold press other than hot press.
  • C more than 0.2% and 0.4% or less
  • the C content is more than 0.2%, preferably 0.22% or more, more preferably 0.24% or more.
  • the C content is preferably 0.4% or less, preferably Is 0.38% or less, more preferably 0.36% or less.
  • Si 0.8% to 1.4%
  • Si is one of the important elements in the present invention. Si can improve the adhesion of the scale after quenching and prevent scale peeling. Moreover, since hardenability improves by containing Si, the hardness of a quenching member can be improved. In order to effectively exhibit such an action, the Si content is 0.8% or more, preferably 0.9% or more, more preferably 1% or more. However, when the Si content is excessive, retained austenite is likely to be generated, which promotes the diffusion of Mn into the retained austenite, and as a result, the Mn concentration in the steel sheet tends to be non-uniform. Therefore, the Si content is 1.4% or less, preferably 1.35% or less, more preferably 1.3% or less.
  • Mn is an element that contributes to increasing the hardness of the quenched member.
  • the Mn content is 1% or more, preferably 1.1% or more, more preferably 1.2% or more.
  • the Mn content is 3% or less, preferably 2.8% or less, more preferably 2.6% or less.
  • P more than 0% and 0.02% or less
  • P is an element inevitably contained, and is an element that deteriorates the weldability of the steel sheet. Therefore, the P content is 0.02% or less, preferably 0.018% or less, more preferably 0.017% or less.
  • the P content may be over 0%, but industrially it is 0.0005% or more.
  • S is an element that is inevitably contained, and is an element that degrades the weldability of the steel sheet. Further, when S is contained, MnS is generated in the steel sheet. As a result, the homogeneity of the concentration distribution of Mn is lowered, and Mn is segregated. Therefore, the S content is 0.002% or less, preferably 0.0018% or less, more preferably 0.0015% or less. Since the S content should be as low as possible, it should be over 0%, but industrially it is 0.0001% or more.
  • sol. Al is an element that acts as a deoxidizer. In order to effectively exhibit such an action, sol.
  • the Al content is 0.02% or more, more preferably 0.025% or more. However, sol. When the Al content is excessive, the hardness of the quenched member is lowered.
  • the Al content is 0.06% or less, preferably 0.055% or less, more preferably 0.05% or less.
  • N more than 0% and 0.01% or less
  • N is an element inevitably contained, and when the N content is excessive, boride is generated and the B content is reduced, so that the hardenability of the steel sheet may be lowered. Therefore, the N content is 0.01% or less, preferably 0.008% or less, more preferably 0.005% or less. In addition, since it is better that the N content is as small as possible, the N content may be over 0%, but industrially it is 0.0001% or more.
  • O is an element inevitably contained, and an element that causes a decrease in the T-direction bendability of the quenched member when included in excess. Therefore, the O content is 0.01% or less, preferably 0.005% or less, more preferably 0.003% or less. In addition, since it is better that the O content is as small as possible, it may be over 0%, but industrially it is 0.0001% or more.
  • B is an element that improves the hardenability of the steel sheet.
  • the B content is 0.0005% or more, preferably 0.001% or more, more preferably 0.0012% or more, and further preferably 0.0015% or more.
  • the B content is 0.005% or less, preferably 0.004% or less, more preferably 0.0035. % Or less.
  • Ti can suppress the decrease in the B content by generating TiN, and can improve the hardenability of the steel sheet by B. Therefore, the Ti content is 0.005% or more, preferably 0.01% or more, more preferably 0.015% or more. However, when it contains excessively, a carbide will precipitate in a grain boundary and the hardenability of a steel plate will deteriorate. Therefore, the Ti content is 0.1% or less, preferably 0.08% or less, more preferably 0.06% or less.
  • the steel sheet for quenching satisfies the above component composition, and the balance is iron and inevitable impurities.
  • an unavoidable impurity for example, not only P, S, N, and O which may be brought into the steel depending on the situation of raw materials, materials, manufacturing equipment, etc., but Pb , Bi, Sb, and Sn may be included.
  • the inevitable impurities here are impurities other than the above P, S, N, and O, and examples thereof include Trump elements such as Pb, Bi, Sb, and Sn.
  • One type, (B) Nb: more than 0% and 0.1% or less, and V: at least one selected from the group consisting of more than 0% and 0.1% or less may be contained.
  • These elements (A) and (B) can be contained alone or in combination with the element described in (A) and the element described in (B). The reason for setting this range is as follows.
  • Cr and Mo are both effective elements for improving the hardenability and improving the strength of the quenched member, and can be used alone or in combination.
  • the Cr and Mo contents are each more than 0%, preferably 0.1% or more, more preferably 0.3% or more.
  • the contents of Cr and Mo are preferable when each is contained alone. Is 3% or less, more preferably 2.5% or less, and still more preferably 2% or less.
  • Nb and V are both effective elements for forming carbides in the steel sheet and improving the strength of the quenched member, and can be used alone or in combination.
  • the contents of Nb and V are each over 0%, preferably 0.005% or more, more preferably 0.008% or more.
  • the contents of Nb and V are each preferably 0.1% or less, more preferably 0.08% or less, and still more preferably 0.06% or less.
  • the present inventors appropriately control the Mn concentration distribution to be within the range of the following formula (1), that is, quenching by suppressing segregation of Mn. It was derived that a quenched member excellent in T-direction bendability can be obtained even in a high strength region where the later hardness is 515 HV or higher. That is, quenching is performed by setting the steel sheet thickness 1/4 position (the position of 1/4 t portion of the steel sheet for quenching with thickness t, the same applies hereinafter) to a steel sheet for quenching that satisfies the following formula (1). It has been clarified that despite the high hardness of the member, it exhibits good T-direction bendability. In addition, the evaluation method of T direction bendability is mentioned later.
  • [Mn] Mn concentration (% by mass) of the steel sheet analyzed by inductively coupled plasma emission spectroscopy
  • S1 Area% of the region where the Mn concentration analyzed by the electron microprobe analyzer is more than twice the above [Mn] in the structure of the steel plate at the thickness 1/4 position.
  • S2 Area% of a region in which the Mn concentration analyzed by an electron beam microprobe analyzer is 0.5 times or less of the above [Mn] in the structure of the steel plate with a thickness of 1/4.
  • Mn segregation means the area% (S1) of the region that is twice or more the Mn concentration of the base material (quenched steel plate) and 0.5 times or less the Mn concentration of the base material. It means that the sum (S1 + S2 (area%)) with the area% (S2) of the region is large. A method for obtaining S1 + S2 (area%) will be described later.
  • the Mn concentration [Mn] of the base material is calculated by chemically analyzing the quenching steel plate by inductively coupled plasma emission spectroscopy. That is, [Mn] is an average value of Mn concentration in the whole steel plate.
  • the present inventors must further suppress the segregation of Mn when the Mn concentration of the base material is higher than when the Mn concentration of the base material is low. Also derived. For example, when [Mn] is 1.3 mass%, S1 + S2 may be less than 31 area%, but when [Mn] is 2.3 mass%, S1 + S2 must be less than 21 area%. .
  • the value of S1 + S2 only needs to be smaller than the value of ⁇ 10 ⁇ [Mn] +44, but since the lower limit of the Mn content is 1%, it is preferably less than 34 area%, and is 31 area% or less. Is more preferably 25% by area or less, and particularly preferably 21% by area or less.
  • the lower limit is not particularly limited and may be 0 area%, but is industrially 5 area% or more, and practically 10 area% or more.
  • S1 + S2 only needs to be smaller than the value of ⁇ 10 ⁇ [Mn] +44. That is, ⁇ 10 ⁇ [Mn] + 44 ⁇ (S1 + S2) only needs to be larger than zero. Further, ⁇ 10 ⁇ [Mn] + 44 ⁇ (S1 + S2) is preferably 1.0 or more, and more preferably 2.0 or more. Further, ⁇ 10 ⁇ [Mn] + 44 ⁇ (S1 + S2) is preferably 10 or less, and more preferably 5.0 or less.
  • the area ratio of ferrite with respect to the entire structure is preferably 50% or less.
  • the area ratio of ferrite with respect to the entire structure is more preferably less than 50%, further preferably 45% or less, and still more preferably 30% or less.
  • the amount of ferrite is preferably small, and may be 0%.
  • the area ratio of the ferrite is measured by observing the position of the steel sheet with a thickness of 1/4 with an optical microscope or a scanning electron microscope (SEM). In some cases, precipitation of carbides may be observed in the ferrite grains. In that case, the ferrite area ratio may be measured including the carbides, assuming that there are no carbides. That is, the ferrite area ratio does not change due to precipitation of carbide.
  • the main structure is preferably a structure other than ferrite.
  • the main structure is pearlite, bainite, and martensite (including autotemper martensite).
  • a tempered martensite is 0%.
  • hot rolling is performed using steel having the above-described component composition.
  • cooling is performed at an average cooling rate [R] (° C./s) from the finish rolling temperature to the winding temperature, and winding is performed at the winding temperature [T] (° C.). take.
  • winding hold at a temperature from the winding temperature to “winding temperature ⁇ 50 ° C.” for [t] time.
  • the above [R], [t], and [T] need to satisfy the following formula (2).
  • the average cooling rate [R] is preferably 10 ° C./s or more, more preferably 15 ° C./s or more.
  • the upper limit of the average cooling rate [R] is not particularly limited, but is industrially preferably 200 ° C./s or less, more preferably 100 ° C./s or less, and 50 ° C./s or less. Is more preferable.
  • the finish rolling temperature is not particularly limited as long as it is an austenite region, but it is preferably at least the Ar 3 transformation point from the viewpoint of suppressing an increase in hot deformation resistance. Moreover, it is preferable that it is 950 degrees C or less from a viewpoint of suppressing scale generation according to a conventional method.
  • Winding temperature [T] (° C)>
  • the coiling temperature is high, untransformed austenite is likely to be generated, which promotes the diffusion of Mn into the untransformed austenite, and as a result, the Mn concentration in the steel sheet may become uneven.
  • winding temperature [T] becomes like this.
  • it is 320 degreeC or more and 650 degrees C or less, More preferably, it is 350 degreeC or more and 600 degrees C or less.
  • the holding time [t] in the above temperature range is preferably 15 hours or less, more preferably 10 hours or less. If the holding time at the temperature from the coiling temperature to the coiling temperature ⁇ 50 ° C. is too long, Mn tends to segregate. Moreover, the lower limit of the holding time [t] is not particularly limited, but is preferably 0.25 hours or more industrially.
  • the “holding” does not necessarily have to be held at the same temperature, and may be varied as long as it is within the above temperature range.
  • the temperature may be kept constant within the above temperature range, or changes within this range, that is, temperature increase due to temperature decrease or heating, temperature increase due to recuperation due to transformation, and the like may be included.
  • the temperature is kept at the above temperature range for a predetermined time, and then cooled to room temperature, but the cooling rate at that time is not particularly limited, and may be air cooling, for example.
  • plating After the hot rolling, plating may be performed if the temperature of the steel sheet in the production process is 300 ° C. or less.
  • a hardened member having a high strength of 515 HV or more and excellent in T-direction bendability can be obtained.
  • the quenching member has high strength after quenching of 515 HV or more and excellent in T-direction bendability.
  • the hardness of the quenched member is preferably 525 HV or more, and more preferably 535 HV or more.
  • the upper limit of the hardness of the quenched member is not particularly limited, but is, for example, 680 HV or less, preferably 650 HV or less, more preferably 600 HV or less, and even more preferably 570 HV or less.
  • the quenched member has a relationship between a bending angle obtained by converting a displacement at the maximum load obtained by a bending test in a T-direction bending according to a VDA standard (VDA238-100) defined by the German Automobile Manufacturers Association and the hardness.
  • VDA238-100 VDA standard
  • the value of the following formula (5) showing is preferably larger than 0, more preferably 5 or more.
  • the value of the following formula (5) being greater than 0 indicates that both the hardness and the bending angle are large.
  • the manufacturing method of the quenching member in the case where the steel plate for quenching according to the present embodiment is applied to hot press forming is not particularly limited, and a known method such as a die quench method can be used. Specifically, there is a method in which the steel sheet for quenching is heated to a temperature at which it becomes an austenite single phase to reduce the strength and press forming with a mold in a state where forming is facilitated. More specifically, the steel sheet for quenching according to the present embodiment is heated to a temperature equal to or higher than the Ac 3 point defined by the following formula (3), and then press forming of the steel sheet is started by a mold. After the start of the above, there is a method of cooling up to the range of the Ms point defined by the following formula (4) while securing an average cooling rate of 20 to 300 ° C./s in the mold.
  • the manufacturing method of the quenching member in the case of applying to hot press molding is not particularly limited as long as it satisfies the hardness of 515 HV or higher. After performing, cooling such as air cooling may be performed.
  • the steel sheet for quenching according to the present embodiment can be applied to press forming other than hot pressing, and then quenched to form a quenched member.
  • a quenched member can be manufactured.
  • the steel plate for hardening which concerns on this embodiment to cold press molding after performing cold press, only the part which requires hardness can be hardened with a high frequency etc., and a hardened member can be manufactured.
  • the component composition is mass%, C: more than 0.2% and 0.4% or less, Si: 0.8% or more and 1.4% or less, Mn: 1% or more and 3% or less, P: more than 0% and 0.02% or less, S: more than 0% and 0.002% or less, sol.
  • [Mn] Mn concentration (% by mass) of the steel sheet analyzed by inductively coupled plasma emission spectroscopy
  • S1 Area% of the region where the Mn concentration analyzed by the electron microprobe analyzer is more than twice the above [Mn] in the structure of the steel plate at the thickness 1/4 position.
  • S2 Area% of a region in which the Mn concentration analyzed by an electron beam microprobe analyzer is 0.5 times or less of the above [Mn] in the structure of the steel plate with a thickness of 1/4.
  • the quenching steel sheet has a ferrite area ratio of 0% or more and 50% or less at a 1 ⁇ 4 thickness position of the steel sheet.
  • the quenching steel plate preferably has a composition of mass% and satisfies B: 0.001% or more and 0.005% or less.
  • the quenching steel plate further contains, as other elements, mass%, Cr: more than 0% and 3% or less, Mo: more than 0% and 3% or less, Nb: more than 0% and 0.1% or less, and V: 0%. It is preferable to contain at least one selected from the group consisting of more than 0.1%.
  • Another aspect of the present invention is a quenched member manufactured using the steel sheet for quenching, which has a hardness of 515 HV or more and has excellent T-direction bendability. .
  • Another aspect of the present invention is a method for producing the steel sheet for quenching, which includes a step of satisfying the following formula (2) after performing finish rolling in the austenite region. It is a manufacturing method of a steel plate.
  • the average cooling rate R is preferably 10 ° C./s or more and 200 ° C./s or less.
  • the held time t is 0.25 hours or more and 15 hours or less.
  • the winding temperature T is preferably 320 ° C. or higher and 650 ° C. or lower.
  • the quenching steel plate by using the quenching steel plate, it is possible to provide a quenching member having excellent T-direction bendability even in a high strength region where the hardness after quenching is 515 HV or higher.
  • [Mn concentration distribution] Using the following formula (1), the concentration distribution of Mn was evaluated according to the following criteria, and A evaluation was passed and B evaluation was rejected.
  • the measurement method of [Mn] and the calculation method of S1 + S2 are as follows.
  • [Mn] Mn concentration (% by mass) of the steel sheet analyzed by inductively coupled plasma emission spectroscopy
  • S1 Area% of the region where the Mn concentration analyzed by the electron microprobe analyzer is more than twice the above [Mn] in the structure of the steel plate at the thickness 1/4 position.
  • S2 Area% of a region in which the Mn concentration analyzed by an electron beam microprobe analyzer is 0.5 times or less of the above [Mn] in the structure of the steel plate with a thickness of 1/4.
  • Measurement area X 300 points Y: 240 points Feed: 0.4 ⁇ m Beam diameter setting: Zero Acquisition time: 20 msec / point Electron beam acceleration voltage: 15 kV Irradiation current: 1 ⁇ 10 ⁇ 6 A (1 ⁇ A) Next, the Mn concentration at each point measured under the above conditions is divided by [Mn], the number of points at which the Mn concentration is 2 times or more of [Mn], and the Mn concentration is 0.5 times or less of [Mn]. A certain number of points was obtained.
  • the total value of the number of points where the Mn concentration is 2 times or more of [Mn] and the number of points where the Mn concentration is 0.5 times or less of [Mn] is the total number of measurement points (300 ⁇ 240 points). Then, S1 + S2 (area%) was calculated.
  • the quenching test was performed under the following conditions using a die quench method simulating a mold.
  • Plate temperature of steel plate for quenching 900 ° C Heating time: 100 seconds Cooling time: about 15 seconds Die quench start temperature: 700 ° C Die quench load: 2000kgf Molded bottom dead center retention time: 30 seconds
  • the T-direction bendability of the quenched member was evaluated under the following measurement conditions based on the VDA standard (VDA238-100) defined by the German Automobile Manufacturers Association.
  • VDA238-100 the displacement at the maximum load obtained in the bending test was converted into an angle based on the VDA, and the bending angle was obtained.
  • the correlation is generally such that the higher the hardness of the quenched member, the lower the bending angle, the T-direction bendability was evaluated based on the magnitude of the bending angle with respect to the hardness of the quenched member.
  • the T-direction bendability was evaluated according to the following criteria based on the value of the following formula (5), and A evaluation was determined to be acceptable ( ⁇ ), and B evaluation was determined to be unacceptable (x). Moreover, the relationship between the hardness [hardness after quenching (HV)] and the bending angle [bending angle after quenching (°)] of each quenched member is shown in FIG.
  • the steel sheets other than the above did not satisfy the component composition or manufacturing conditions defined in the present invention, and the desired characteristics could not be obtained.
  • a quenching member having excellent T-direction bendability is provided even in a high strength region where the hardness after quenching is 515 HV or higher.

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Abstract

Un aspect de la présente invention concerne une tôle d'acier destinée à être durcie, caractérisée en ce qu'elle satisfait une composition de composants prescrite et dont la concentration de Mn satisfait la formule (1). S1+S2 <− 10 × [Mn] + 44 (1). [Mn] : concentration de Mn (% en poids) de la tôle d'acier, analysée par spectroscopie d'émission de plasma à couplage inductif. S1 : dans la structure de la tôle d'acier, au niveau de la position correspondant au quart de l'épaisseur de la tôle, le % en surface des régions dans lesquelles la concentration de Mn, analysée par un analyseur à microsonde électronique, est d'au moins 2 fois [Mn]. S2 : dans la structure de la tôle d'acier, au niveau de la position correspondant au quart de l'épaisseur de la tôle, le % en surface des régions dans lesquelles la concentration de Mn, analysée par un analyseur à microsonde électronique, n'est pas supérieure à 0,5 fois [Mn].
PCT/JP2017/002186 2016-02-29 2017-01-23 Tôle d'acier destinée à être durcie, élément durci et procédé de fabrication de tôle d'acier destinée à être durcie Ceased WO2017149999A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
CN201780013823.XA CN108779527A (zh) 2016-02-29 2017-01-23 淬火用钢板、淬火构件、以及淬火用钢板的制造方法
MX2018010347A MX2018010347A (es) 2016-02-29 2017-01-23 Hoja de acero para proceso de templado, elemento endurecido, y metodo para la fabricacion de hoja de acero para proceso de templado.
BR112018067894A BR112018067894A2 (pt) 2016-02-29 2017-01-23 chapa de aço para endurecimento, elemento endurecido e método para fabricação de chapa de aço para endurecimento
CA3015966A CA3015966A1 (fr) 2016-02-29 2017-01-23 Tole d'acier destinee a etre durcie, element durci et procede de fabrication de tole d'acier destinee a etre durcie
US16/080,566 US20190017142A1 (en) 2016-02-29 2017-01-23 Steel sheet for hardening, hardened member, and method for manufacturing steel sheet for hardening
EP17759471.0A EP3421631A4 (fr) 2016-02-29 2017-01-23 Tôle d'acier destinée à être durcie, élément durci et procédé de fabrication de tôle d'acier destinée à être durcie
KR1020187026939A KR20180117127A (ko) 2016-02-29 2017-01-23 담금질용 강판, 담금질 부재, 및 담금질용 강판의 제조 방법

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