WO2025142033A1 - 鋼板、部材およびそれらの製造方法 - Google Patents

鋼板、部材およびそれらの製造方法 Download PDF

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WO2025142033A1
WO2025142033A1 PCT/JP2024/036362 JP2024036362W WO2025142033A1 WO 2025142033 A1 WO2025142033 A1 WO 2025142033A1 JP 2024036362 W JP2024036362 W JP 2024036362W WO 2025142033 A1 WO2025142033 A1 WO 2025142033A1
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temperature
ferrite
steel sheet
steel
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English (en)
French (fr)
Japanese (ja)
Inventor
洋一郎 松井
三周 知場
琴未 野口
英之 木村
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2025511874A priority Critical patent/JP7772274B1/ja
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • C 0.06% or more and 0.25% or less C is contained from the viewpoint of securing the area ratio of tempered martensite to secure a predetermined strength, securing the area ratio (volume ratio) of retained austenite (retained ⁇ ) to improve ductility, and concentrating in the retained ⁇ to stabilize the retained ⁇ to improve ductility. If the C content is less than 0.06%, these effects cannot be sufficiently secured, so the lower limit is set to 0.06%.
  • the C content is preferably 0.09% or more, and more preferably 0.11% or more.
  • the upper limit of the C content is set to 0.25%.
  • the C content is preferably set to 0.22% or less.
  • the C content is more preferably set to 0.20% or less.
  • the chemical conversion treatability and the toughness of the welded parts may deteriorate.
  • the Si content is set to 2.5% or less.
  • the Si content is preferably less than 2.0%.
  • the Si content is preferably 1.8% or less, and more preferably 1.5% or less.
  • Mn 1.5% or more and 3.5% or less
  • Mn is an important element from the viewpoint of securing a predetermined area ratio of tempered martensite and/or bainite to secure strength, and from the viewpoint of stabilizing residual ⁇ by lowering the Ms point of residual ⁇ to improve ductility.
  • Mn is also an important element from the viewpoint of suppressing the generation of carbides in bainite to improve ductility, similar to Si, and from the viewpoint of increasing the volume fraction of residual ⁇ to improve ductility.
  • the Mn content is set to 1.5% or more. From the viewpoint of stabilizing residual ⁇ to improve ductility, the Mn content is preferably 2.5% or more.
  • the Mn content is more preferably 2.6% or more, and even more preferably 2.7% or more.
  • the bainite transformation is significantly delayed, resulting in a decrease in ductility.
  • the Mn content exceeds 3.5%, it becomes difficult to suppress the formation of coarse aggregated ⁇ and coarse aggregated martensite, and the stretch flange formability is also deteriorated.
  • the Mn content exceeds 3.5%, the hardenability increases excessively, and therefore the amount of ferrite having a solute Mn content of 2.0 mass% or more, which is generated in the step of cooling the temperature range from the annealing temperature to the annealing temperature -15°C at an average cooling rate CR1 of 0.01°C/s to 5°C/s, becomes insufficient, and sufficient energy absorption characteristics during collision may not be obtained. Therefore, the Mn content is set to 3.5% or less. From the viewpoint of ensuring high ductility and energy absorption characteristics during a collision by promoting ferrite transformation and bainite transformation, the Mn content is preferably set to 3.2% or less, and more preferably set to 3.1% or less.
  • P 0.10% or less
  • P is an element that strengthens steel, but if its content is high, it deteriorates spot weldability. Therefore, the P content is set to 0.10% or less.
  • the P content is preferably set to 0.02% or less. From the viewpoint of improving spot weldability, the P content is more preferably set to 0.01% or less. Note that P may not be contained, but from the viewpoint of manufacturing costs, the P content is preferably 0.001% or more.
  • S 0.010% or less
  • S has the effect of improving scale peeling during hot rolling and suppressing nitriding during annealing, but is an element that has a negative effect on spot weldability, bendability, and hole expandability.
  • the S content is set to 0.010% or less.
  • the high content of C, Si, and Mn tends to deteriorate spot weldability, so from the viewpoint of improving spot weldability, the S content is preferably set to 0.0020% or less, and more preferably set to less than 0.0010%.
  • the S content is preferably 0.0001% or more from the viewpoint of production costs, and more preferably 0.0005% or more.
  • Sol. Al 1.0% or less Al is contained for the purpose of deoxidation or to stabilize residual ⁇ as a substitute for Si.
  • the sol. Al content is preferably 0.005% or more.
  • the sol. Al content is more preferably 0.01% or more, even more preferably 0.02% or more, and even more preferably 0.03% or more.
  • the sol. Al content is set to 1.0% or less.
  • the sol. Al content is preferably less than 0.50%, more preferably 0.20% or less.
  • the sol. Al content is further preferably 0.15% or less, and even more preferably 0.10% or less.
  • N 0.015% or less
  • N is an element that forms nitrides such as BN, AlN, TiN, etc. in steel, and is an element that reduces the hot ductility of steel and reduces surface quality.
  • the N content is set to 0.015% or less.
  • the N content is preferably 0.010% or less.
  • the N content is preferably 0.0001% or more from the viewpoint of production costs, and more preferably 0.001% or more.
  • the balance other than the above is Fe and unavoidable impurities. It is preferable that the steel sheet of the present invention has a composition containing the above basic components, with the balance being Fe and unavoidable impurities.
  • Cr 1.0% or less Cr can be included to improve the hardenability of steel and to suppress the formation of carbides in martensite and upper/lower bainite.
  • the Cr content is preferably 0.01% or more.
  • the Cr content is more preferably 0.03% or more, and further preferably 0.06% or more.
  • the Cr content is set to 1.0% or less.
  • the Cr content is preferably 0.8% or less, more preferably 0.4% or less.
  • the Cr content is further preferably 0.2% or less, and even more preferably 0.1% or less.
  • Mo 0.5% or less Mo can be added due to its effect of improving the hardenability of steel and its effect of suppressing the formation of carbides in martensite and upper/lower bainite.
  • the Mo content is preferably 0.01% or more, more preferably 0.03% or more, and further preferably 0.06% or more.
  • the Mo content is set to 0.5% or less. From the viewpoint of improving the chemical conversion treatability, the Mo content is preferably set to 0.15% or less.
  • V 0.5% or less V can be added due to its effects of improving the hardenability of steel, suppressing the formation of carbides in martensite and upper/lower bainite, refining the structure, and precipitating carbides to improve delayed fracture resistance.
  • the V content is preferably 0.003% or more, more preferably 0.005% or more, and even more preferably 0.010% or more.
  • the V content is set to 0.5% or less, preferably 0.3% or less, more preferably 0.1% or less, and further preferably 0.05% or less.
  • Nb 0.1% or less Nb can be added due to its effects of refining the steel structure to increase strength, promoting bainite transformation through grain refinement, improving bendability, and improving delayed fracture resistance.
  • the Nb content is preferably 0.002% or more.
  • the Nb content is more preferably 0.004% or more, even more preferably 0.010% or more, and even more preferably 0.020% or more.
  • the Nb content is set to 0.1% or less.
  • the Nb content is preferably 0.05% or less, and more preferably 0.03% or less.
  • W 0.2% or less W can be added due to its effects of improving the hardenability of steel, suppressing the formation of carbides in bainite, refining the structure, and precipitating carbides to improve delayed fracture resistance.
  • the W content is preferably 0.005% or more.
  • the W content is more preferably 0.008% or more, and even more preferably 0.010% or more.
  • the W content is set to 0.2% or less.
  • the W content is preferably 0.15% or less, more preferably 0.08% or less, and further preferably 0.05% or less.
  • Ca 0.0040% or less Ca fixes S as CaS and contributes to improving bendability and delayed fracture resistance. Therefore, the Ca content is preferably 0.0002% or more. The Ca content is more preferably 0.0005% or more, and further preferably 0.0010% or more. On the other hand, since the addition of a large amount of Ca deteriorates the surface quality and bendability, when Ca is contained, the Ca content is set to 0.0040% or less, preferably 0.0035% or less, and more preferably 0.0020% or less.
  • Ce 0.0040% or less
  • the Ce content is preferably 0.0002% or more.
  • the Ce content is more preferably 0.0004% or more, and further preferably 0.0006% or more.
  • the Ce content is set to 0.0040% or less, preferably 0.0035% or less, and more preferably 0.0020% or less.
  • La 0.0040% or less Like Ca, La also fixes S and contributes to improving bendability and delayed fracture resistance. For this reason, the La content is preferably 0.0002% or more. The La content is more preferably 0.0004% or more, and further preferably 0.0006% or more. On the other hand, if a large amount of La is added, the surface quality and bendability deteriorate, so when La is contained, the La content is set to 0.0040% or less, preferably 0.0035% or less, and more preferably 0.0020% or less.
  • Mg 0.0030% or less Mg fixes O as MgO and contributes to improving delayed fracture resistance. Therefore, the Mg content is preferably 0.0002% or more. The Mg content is more preferably 0.0004% or more, and further preferably 0.0006% or more. On the other hand, if a large amount of Mg is added, the surface quality and bendability deteriorate, so if Mg is contained, the Mg content is set to 0.0030% or less, preferably 0.0025% or less, and more preferably 0.0010% or less.
  • Sb 0.1% or less Sb suppresses oxidation and nitridation of the surface layer of the steel sheet, thereby suppressing the resulting reduction in the content of C and B in the surface layer. In addition, by suppressing the reduction in the content of C and B, the generation of ferrite in the surface layer of the steel sheet is suppressed, and the strength is increased and the delayed fracture resistance is improved. From this viewpoint, the Sb content is preferably 0.002% or more. The Sb content is more preferably 0.004% or more, and further preferably 0.006% or more.
  • the Sb content is set to 0.1% or less.
  • the Sb content is preferably 0.04% or less, more preferably 0.03% or less, and further preferably 0.02% or less.
  • Area ratio of tempered martensite 20% or more and 80% or less
  • the area ratio of tempered martensite is set to 20% or more.
  • the area ratio of tempered martensite is preferably 30% or more, and more preferably 40% or more.
  • the area ratio of tempered martensite is set to 80% or less, preferably 70% or less, and more preferably 60% or less.
  • the average cooling rate CR2 (°C/s) is calculated by "(annealing temperature (°C)-15 (°C)-cooling stop temperature (°C))/(cooling time (s) from annealing temperature-15°C to cooling stop temperature)".
  • the temperature range of 340°C to 590°C is held for 20s to 3000s at an average cooling rate CR4 of 0.01 to 5°C/s. From the viewpoint of distributing C to the residual ⁇ to stabilize them and improve ductility, and from the viewpoint of subdividing the region distributed in chunks as untransformed ⁇ by bainite transformation and improving ⁇ , the steel is held (slowly cooled) for 20s to 3000s in the temperature range of 340°C to 590°C. Furthermore, in order to suppress the generation of chunky structure due to the distribution of excess C to the residual ⁇ and to improve ⁇ by self-tempering of fresh martensite, this temperature range is slowly cooled at an average cooling rate CR4 of 0.01 to 5°C/s.
  • the average cooling rate CR4 is set to 0.01°C/s or more.
  • the average cooling rate CR4 exceeds 5°C/s, the distribution of C to the residual ⁇ is suppressed, and a sufficient amount of C-enriched region cannot be obtained. In addition, fresh martensite is generated, which leads to deterioration of ⁇ . Therefore, the average cooling rate CR4 is set to 5°C/s or less.
  • the average cooling rate CR4 is calculated by "(cooling start temperature (°C)-cooling stop temperature (°C))/(cooling time (s) from the cooling start temperature to the cooling stop temperature)".
  • the cooling start temperature and the cooling stop temperature are not particularly limited as long as they are in the range of 340° C. to 590° C., but the cooling start temperature is preferably 360° C. or higher.
  • the cooling start temperature is preferably 580° C. or lower.
  • the cooling stop temperature is preferably 350° C. or higher.
  • the cooling stop temperature is preferably 450° C. or lower.
  • the holding (dwelling, slow cooling) in the temperature range of 340°C to 590°C may also serve as a hot-dip galvanizing treatment or an alloyed hot-dip galvanizing treatment. That is, in the step of holding at the average cooling rate CR4: 0.01 to 5°C/s described above, the steel sheet may be subjected to a hot-dip galvanizing treatment or an alloyed hot-dip galvanizing treatment.
  • the hot-dip galvanizing treatment it is preferable to immerse the steel sheet in a galvanizing bath at 440°C to 500°C, perform the hot-dip galvanizing treatment, and then adjust the coating weight by gas wiping or the like.
  • hot-dip galvanizing it is preferable to use a galvanizing bath having an Al content of 0.10% to 0.22%.
  • a galvanizing alloying treatment can be performed after the hot-dip galvanizing treatment.
  • the galvanizing alloying treatment it is preferable to perform it in a temperature range of 470°C to 590°C. This step is a step of cooling (retention and slow cooling (slow cooling)), but as long as the above-mentioned temperature range, retention time range, and average cooling rate CR4 range are satisfied, hot-dip galvanizing treatment or alloying treatment of galvanizing can be performed during this step.
  • Hot-dip galvanizing treatment or alloying treatment of galvanizing may be accompanied by a temperature rise.
  • Cooling is performed at an average cooling rate CR5 of 0.1°C/s or more to a temperature of 50°C or less. Thereafter, cooling is performed at an average cooling rate CR5 of 0.1°C/s or more to a temperature of 50°C or less from the viewpoint of preventing softening due to excessive tempering and a decrease in ductility due to carbide precipitation.
  • the steel plate can be subjected to skin pass rolling.
  • the skin pass elongation rate is preferably 0.1 to 0.5%.
  • the plate shape can also be flattened with a leveler.
  • the average cooling rate CR5 to the temperature of 50°C or less is preferably 5°C/s or more.
  • the average cooling rate CR5 is preferably 100°C/s or less.
  • the average cooling rate CR5 is calculated by (340 (°C) (cooling start temperature) - cooling stop temperature (°C) below 50°C) / (cooling time (s) from cooling start temperature to cooling stop temperature).
  • low-temperature heat treatment In order to improve stretch flange formability, it is also possible to carry out low-temperature heat treatment at 100 to 300°C for 30 seconds to 10 days after the above annealing (heat treatment) or after skin-pass rolling. This treatment tempers the martensite formed during final cooling or skin-pass rolling, and causes hydrogen that entered the steel sheet during annealing to be released from the steel sheet. Low-temperature heat treatment can reduce hydrogen to less than 0.1 ppm.
  • the steel sheet may be subjected to electrogalvanization. After electroplating, it is preferable to apply the above-mentioned low-temperature heat treatment from the viewpoint of reducing hydrogen in the steel.
  • Second embodiment (with retention process)
  • a steel slab having the above-mentioned composition is hot-rolled and cold-rolled, and then the obtained cold-rolled steel sheet is annealed.
  • an average cooling rate CR3 10° C./s for not less than 10 s and not more than 60 s; a step of cooling the steel sheet at an average cooling rate CR2B of 3° C./s or more in a temperature range from the retention stop temperature to a cooling stop temperature of 200° C. or more and 300° C. or less; Heating the material at an average heating rate of 2° C./s or more in a temperature range from the cooling stop temperature to 380° C.; A step of retaining the material in a temperature range of 340° C. or more and 590° C. or less at an average cooling rate CR4: 0.01 to 5° C./s for 20 s to 3,000 s; and cooling to a temperature of 50° C. or less at an average cooling rate CR5: 0.1° C./s or more.
  • the hot rolling and cold rolling can be performed under the same conditions as in the first embodiment.
  • the annealing temperature the process of holding at 775° C. or more and 830° C. or less and the process of cooling at an average cooling rate CR1: 0.01° C./s or more and 5° C./s or less can be performed under the same conditions as in the first embodiment.
  • the process of cooling at an average cooling rate CR2 of 3° C./s or more in the first embodiment is replaced with a process of cooling at an average cooling rate CR2A of 3° C./s or more, a process of retaining the material at an average cooling rate CR3 of 10° C./s or less for 10 s to 60 s, and a process of cooling at an average cooling rate CR2B of 3° C./s or more.
  • the process of heating at an average heating rate of 2° C./s or more, the process of retaining at an average cooling rate CR4 of 0.01 to 5° C./s for 20 s to 3000 s, and the process of cooling at an average cooling rate CR5 of 0.1° C./s or more can be performed under the same conditions as those in the first embodiment.
  • other treatments such as hot dip galvanizing, skin pass rolling, low temperature heat treatment after annealing, and electroplating can also be performed under the same conditions as those in the first embodiment.
  • CR2A a process of cooling at an average cooling rate of 3°C/s or more
  • CR3 a process of retaining the material for 10 s to 60 s at an average cooling rate of 10°C/s or less
  • CR2B a process of cooling at an average cooling rate of 3°C/s or more.
  • Annealing temperature -15°C to 500°C, cooling at an average cooling rate of CR2A: 3°C/s or more. Temperature range from 500°C to the martensitic transformation start temperature Ms or higher and the residence stop temperature of 320°C or higher: 10°C/s or less, residence time of 10 s to 60 s. Temperature range from the residence stop temperature to the cooling stop temperature of 200°C to 300°C, cooling at an average cooling rate of CR2B: 3°C/s or more.
  • a retention (slow cooling) treatment process is included in which the steel is retained in the temperature range from 500°C to a retention stop temperature of 500°C to a martensitic transformation start temperature Ms or more and 320°C or more at an average cooling rate of CR3: 10°C/s or less for 10 s to 60 s.
  • the reason why the average cooling rate CR2A is set to 3° C./s or more and the average cooling rate CR2B is set to 3° C./s or more is the same as the reason why the average cooling rate CR2 is set to 3° C./s or more as described in the first embodiment.
  • Both of the average cooling rates CR2A and CR2B are preferably 5° C./s or more, and more preferably 8° C./s or more.
  • both of the average cooling rates CR2A and CR2B are too large, the plate shape deteriorates, so it is preferable that the average cooling rates CR2A and CR2B are 100° C./s or less.
  • the average cooling rate CR3 (°C/s) is calculated by (500 (°C) - retention stop temperature (°C))/(cooling time from 500°C to retention stop temperature (s)).
  • the martensitic transformation start temperature Ms can be determined by using a cylindrical test piece (diameter 3 mm x height 10 mm) and measuring the change in height of the test piece when it is held at a specified annealing temperature in a Formaster testing machine and then quenched with helium gas.
  • the steel plate of the present invention preferably has a thickness of 0.5 mm or more. Also, the thickness is preferably 2.0 mm or less.
  • the member of the present invention is obtained by subjecting the steel plate of the present invention to at least one of forming and joining processes.
  • the manufacturing method of the member of the present invention also includes a step of subjecting the steel plate of the present invention to at least one of forming and joining processes to form the member.
  • the steel plate of the present invention has a tensile strength of 780 MPa or more, high ductility, excellent stretch flange formability, and excellent energy absorption properties during a collision. Therefore, members obtained using the steel plate of the present invention are also high in strength, and have higher ductility, excellent stretch flange formability, and excellent energy absorption properties during a collision compared to conventional high-strength members. Furthermore, the use of the members of the present invention makes it possible to reduce weight. Therefore, the members of the present invention can be suitably used, for example, for vehicle body frame parts.
  • the members of the present invention also include welded joints.
  • general processing methods such as pressing can be used without restrictions.
  • general welding methods such as spot welding and arc welding, riveting, crimping, etc. can be used without restrictions.
  • Cold rolled steel sheets having the chemical composition shown in Table 1 and a thickness of 1.4 mm were treated under the annealing conditions shown in Table 2 to produce steel sheets according to the present invention and comparative steel sheets.
  • Each cold-rolled steel sheet was obtained by subjecting a steel slab having the chemical composition shown in Table 1 to hot rolling (slab heating temperature: 1200°C, soaking time: 60 min, finish rolling temperature: 900°C, coiling temperature: 500°C) and cold rolling (rolling ratio (cumulative rolling ratio): 50%).
  • the martensitic transformation start temperature Ms was determined by using a cylindrical test piece (diameter 3 mm x height 10 mm) and measuring the change in height of the test piece when it was held at a specified annealing temperature in a Formaster testing machine and then quenched with helium gas.
  • Some of the steel sheets (cold-rolled steel sheets: CR) were subjected to hot-dip galvanizing treatment in a process in which the steel sheets were retained in a temperature range of 340°C to 590°C for 20 s to 3000 s at an average cooling rate of CR4: 0.01 to 5°C/s, to produce hot-dip galvanized steel sheets (GI).
  • GI hot-dip galvanized steel sheets
  • the steel sheets were immersed in a zinc plating bath at 440°C to 500°C to produce hot-dip galvanized steel sheets, and then the coating weight was adjusted by gas wiping or the like.
  • a zinc plating bath with an Al content of 0.10% to 0.22% was used for hot-dip galvanizing.
  • CR2A and CR2B are both equal to CR2B, and CR2A and CR2B are collectively shown as CR2 in Table 2.
  • JIS No. 5 tensile test pieces and hole expansion test pieces were taken from the obtained steel plate, and tensile tests (in accordance with JIS Z2241 (2011)) were performed.
  • TS and T-El are shown in Table 3. Those having a tensile strength of 780 MPa or more were judged to have excellent strength.
  • the total elongation T-El was judged to be excellent in ductility when it was 18.0% or more when TS was less than 980 MPa, 16.0% or more when TS was 980 MPa or more and less than 1180 MPa, 14.0% or more when TS was 1180 MPa or more and less than 1320 MPa, and 13.0% or more when TS was 1320 MPa or more.
  • the stretch flange formability was evaluated by a hole expansion test specimen taken from the steel plate obtained after heat treatment and a hole expansion test in accordance with the provisions of the Japan Iron and Steel Federation standard JFST1001. That is, after punching a sample of 100 mm x 100 mm square size using a punching tool with a punch diameter of 10 mm and a die diameter of 10.3 mm (clearance 13%), a conical punch with an apex angle of 60 degrees was used to expand the hole until a crack penetrating the plate thickness occurred, with the burrs generated during the punching hole formation being on the outside.
  • the examples of the present invention shown in Tables 2 and 3 are excellent in strength, ductility, stretch flange formability, and energy absorption properties, while the comparative examples are inferior in all of these areas.
  • the steel plate of the present invention was used to produce components obtained by forming, joining, and further to produce components by forming and joining, and that because the steel plate of the present invention has high strength, high ductility, excellent stretch flange formability, and excellent energy absorption properties during a collision, it has the same high strength, high ductility, excellent stretch flange formability, and excellent energy absorption properties during a collision as the steel plate of the present invention.

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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013089095A1 (ja) * 2011-12-15 2013-06-20 株式会社神戸製鋼所 強度および延性のばらつきの小さい高強度冷延鋼板およびその製造方法
WO2018216522A1 (ja) * 2017-05-24 2018-11-29 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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