WO2014162661A1 - Cold-rolled steel sheet and manufacturing method therefor - Google Patents
Cold-rolled steel sheet and manufacturing method therefor Download PDFInfo
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- WO2014162661A1 WO2014162661A1 PCT/JP2014/001265 JP2014001265W WO2014162661A1 WO 2014162661 A1 WO2014162661 A1 WO 2014162661A1 JP 2014001265 W JP2014001265 W JP 2014001265W WO 2014162661 A1 WO2014162661 A1 WO 2014162661A1
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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
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0242—Flattening; Dressing; Flexing
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Definitions
- the present invention is suitable for materials such as plates, disks, and rings that are automotive drive-train parts, and is suitable for materials such as punchability and heat distortion characteristics (heat).
- the present invention relates to a cold-rolled steel sheet having excellent strain resistance and a method for producing the same.
- Plates, disks, rings, etc. (such as AT plates, etc.) used as automotive drive system parts have conventionally been quenched for the purpose of hardening after steel plates are punched into a predetermined shape.
- the heat treatment is performed to adjust the hardness to a predetermined level, and then a friction material is adhered.
- a great amount of heat energy is consumed for the heat treatment, and a dedicated heat treatment facility is required, so an increase in production cost is inevitable.
- Patent Document 1 in mass%, C: 0.05 to 0.6%, Si: 2.0% or less, Mn: 0.2 to 2.0%, P: 0.03% or less, S: 0.03% or less, Sol.Al: 0.1% or less , N: Steel containing less than 0.01%, balance Fe and inevitable impurities, hot-rolled at a finish temperature (Ar 3 transformation point –20 ° C) or higher, cooling rate over 120 ° C / second, cooling stop temperature Cooling is performed so that the difference in cooling stop temperature between the center part and the edge part in the width direction of the steel sheet is 650 ° C or lower, and the cooling temperature is 30 ° C or lower.
- Patent Document 2 includes mass%, C: 0.05 to less than 0.10%, Si: 0.5% or less, Mn: 0.20 to 2.0%, P: 0.03% or less, S: 0.020% or less, Cr: 0.05 to 0.5%
- the steel material with the balance consisting of Fe and inevitable impurities is hot-rolled with the finish rolling finish temperature of finish rolling set to the Ar 3 transformation point or higher, and cooled to 500-650 ° C within 8 s after finish rolling. , Having a base made of pro-eutectoid ferrite, pearlite, bainitic ferrite or bainite, after being wound at 500 to 650 ° C.
- a technique for producing a cold-rolled steel sheet by performing cold rolling of up to 70% has been proposed. And according to the technique proposed by patent document 2, it is supposed that the cold-rolled steel plate excellent in the flatness after stamping and excellent in the end surface property will be obtained.
- Patent Document 3 C: 0.15 to 0.25 mass%, Si: 0.25 mass% or less, Mn: 0.3 to 0.9 mass%, P: 0.03 mass% or less, S: 0.015 mass% or less, Al: 0.01 to 0.08 mass% , N: 0.008% by mass or less, Ti: 0.01-0.05% by mass, B: 0.002-0.005% by mass, with the balance being substantially Fe composition, hot rolling finish temperature: Ar 3 Hot rolling at a transformation point or higher, coiling temperature: 500-600 ° C, hot-rolled steel sheet pickled, then cold rolled at a reduction rate of 50% or higher without annealing, and diameter of 300mm or higher A technique for manufacturing a cold-rolled steel sheet has been proposed by performing light reduction rolling with a reduction ratio of 1% or less using this roll. According to the technique proposed in Patent Document 3, it is said that a cold rolled steel sheet for automatic transmission with reduced residual stress generated during cold rolling can be obtained.
- the C content is as high as 0.15 to 0.25% by mass and the coiling temperature in the hot rolling process is as low as 500 to 600 ° C. Generate. Therefore, as in the technique proposed in Patent Document 2, the residual stress inside the steel sheet increases during cold rolling. As a result, even if a flat shape is obtained in the state of punching, heat is generated by heating after punching. There was a problem that distortion occurred.
- the object of the present invention is to solve the above-mentioned problems and to provide a cold-rolled steel sheet having hardness necessary for drive system parts such as a plate and a disk, flatness after punching, punched end face properties, and heat-resistant strain characteristics, and its It is to provide a manufacturing method.
- the heat-resistant strain property means that when the friction material is heated to a temperature range of about 100 to 400 ° C in the adhesion process of the friction material or in an actual use environment, the thin steel sheet is less deformed and sufficient flatness is obtained. Means a characteristic.
- the present inventors conducted extensive research on various factors that affect the heat-resistant strain characteristics, flatness after punching, and punched end surface properties of cold-rolled steel sheets.
- the rolling reduction in cold rolling is set to a predetermined value or less, and the C content of the steel material is reduced to a predetermined value or less and hot rolling is performed.
- the hot-rolled sheet before cold rolling is the ferrite main phase, the volume fraction of the pearlite phase and bainite phase of the hot-rolled sheet is reduced, and after cold rolling It was found that it is important to control the average grain size and average aspect ratio of the pearlite and bainite phases of the steel sheet.
- the hot-rolled sheet before cold rolling is a pearlite phase or a bainite phase that is a hard phase together with ferrite as a main phase (hereinafter, either one of the pearlite phase or the bainite phase may be referred to as a “hard phase”).
- a pearlite phase or a bainite phase that is a hard phase together with ferrite as a main phase
- either one of the pearlite phase or the bainite phase may be referred to as a “hard phase”.
- the hot-rolled sheet before cold rolling is used as a ferrite main phase, and the volume fraction of the hard phase contained in the hot-rolled sheet is reduced, so that the vicinity of the ferrite / pearlite interface during cold rolling, or ferrite / Residual stress accompanying non-uniform deformation near the interface of bainite can be reduced, and the thermal strain characteristics of the cold-rolled steel sheet can be improved. If such a cold-rolled steel plate is used to manufacture drive system parts such as plates, it will be obvious that after punching into a predetermined shape, even if it is exposed to high temperatures in the bonding process with friction materials or in the actual usage environment, The problem of a decrease in flatness due to strain can be solved.
- the present inventors use a hot rolled sheet before cold rolling as a ferrite main phase, lower the volume fraction of the hard phase of the hot rolled sheet, and control the average grain size and average aspect ratio of the hard phase. Has been found to be extremely effective in improving the flatness after punching of the cold-rolled steel sheet and the properties of the punched end face.
- the hard phase In cold rolling, the hard phase is extended in the rolling direction, but the hardness difference between the main phase ferrite and the hard phase is large, so the hard phase extends in the rolling direction (that is, the aspect ratio of the hard phase).
- the strain accumulated at the interface between the ferrite phase and the hard phase increases, residual stress accumulates, and the heat-resistant strain characteristics of the cold-rolled steel sheet deteriorate. Therefore, in order to improve these characteristics, it is necessary to make the average aspect ratio of the hard phase composed of at least one of the pearlite and bainite phases below a predetermined value.
- the average particle size of the hard phase to a predetermined value or less, even if cracks occur from the boundary interface (boundary between different phases), it prevents the cracks from propagating greatly and punches without defects. An end face is obtained.
- the C content of the steel material is reduced to a predetermined value or less.
- the present invention has been completed based on the above findings, and the gist of the present invention is as follows.
- the area ratio of the ferrite phase is 80% or more, and from one or more of pearlite phase and bainite phase
- the hard phase has a total area ratio of 20% or less, an average particle size of the hard phase of 1 ⁇ m to 10 ⁇ m, and an average aspect ratio of the hard phase of 10.0 or less, and a Vickers hard A cold-rolled steel sheet having a Vickers hardness of Hv170 or more and excellent in punchability and thermal strain characteristics.
- the punching property and heat resistance further include at least one of Cu: 0.01% to 0.20% and Ni: 0.01% to 0.50% in mass%. Cold rolled steel sheet with excellent strain characteristics.
- any one or more of Sb: 0.001% to 0.030%, Sn: 0.001% to 0.030% or less A cold-rolled steel sheet excellent in punchability and heat distortion characteristics.
- the composition further contains at least one of Cu: 0.01% or more and 0.20% or less, Ni: 0.01% or more and 0.50% or less.
- any one or more of Ca: 0.0003% to 0.0050%, REM: 0.0003% to 0.0100% The manufacturing method of the cold-rolled steel plate excellent in the punchability and heat-strain-resistant characteristic containing this.
- a cold-rolled steel sheet having excellent heat-resistant strain characteristics can be easily produced, and a remarkable industrial effect can be achieved.
- the cold-rolled steel sheet according to the present invention is extremely suitable as a material for driving parts such as automobile parts, particularly plates and disks.
- % which is a unit of each component element content, means mass%.
- C 0.01% or more and 0.08% or less C is an element necessary for strengthening steel sheets.
- the C content is 0.01% or more. There is a need to.
- the upper limit of C content is 0.08%.
- the C content is preferably less than 0.05%. More preferably, it is 0.04% or less.
- Si 0.01% or more and 1.0% or less
- Si is a deoxidizer for steel and has the effect of improving the cleanliness of the steel, so the content is made 0.01% or more.
- Si is also an element that increases the hardness of the steel sheet by solid solution hardening, and can be added to obtain a desired hardness.
- the Si content exceeds 1.0%, the surface quality of the steel sheet deteriorates, so the upper limit of the Si content is 1.0%.
- a plate material used for a component that generates friction is required to have good surface properties, and therefore, it is preferably set to 0.6% or less.
- Mn 0.05% or more and 1.0% or less
- Mn is an element that increases the hardness of the steel sheet by solid solution strengthening, and the Mn content needs to be 0.05% or more in order to obtain a desired hardness. Preferably it is 0.1% or more. If the Mn content exceeds 1.0%, in addition to excessive generation of pearlite, bainite, etc., pearlite and the like are generated in layers due to segregation, and the punched end face properties deteriorate. Therefore, the Mn content is 1.0% or less. Preferably it is 0.5% or less.
- P 0.03% or less
- P is an element that is easily segregated in steel. When it is contained in a large amount, the formation of a layered structure is promoted by the segregation of P, and the punched end face properties deteriorate. Therefore, the P content needs to be 0.03% or less. Preferably it is 0.02% or less.
- S 0.015% or less S forms sulfide inclusions such as MnS and degrades the punched end face properties. Therefore, the S content needs to be 0.015% or less. Preferably it is 0.010% or less.
- Al 0.005% or more and 0.10% or less Since Al can improve the cleanliness of the steel sheet by adding it as a deoxidizing element, its content needs to be 0.005% or more. Preferably it is 0.03% or more. On the other hand, if the Al content exceeds 0.10%, oxides are excessively generated, the surface properties are deteriorated, and the adhesion to the friction material is deteriorated. Therefore, the Al content is 0.10% or less. Preferably it is 0.08% or less.
- N 0.01% or less N is a harmful element in the present invention, and if its content is excessive, the ductility of the steel sheet is lowered and the punched end face properties are deteriorated. Therefore, the N content is 0.01% or less. Preferably it is 0.006% or less.
- the cold-rolled steel sheet of the present invention can contain the following elements as necessary in addition to these basic components.
- Cu 0.01% or more and 0.20% or less
- Ni 0.01% or more and 0.50% or less
- the Cu content is 0.01% or more and the Ni content is 0.01% or more. More preferably, the Cu content is 0.02% or more, and the Ni content is 0.02% or more.
- the Cu content is preferably 0.20% or less and the Ni content is preferably 0.50% or less. More preferably, the Cu content is 0.10% or less, and the Ni content is 0.30% or less.
- Ti 0.005% to 0.10%, Nb: 0.005% to 0.10%, V: 0.005% to 0.50%, Zr: 0.005% to 0.10%, Mo: 0.02% to 0.50%, Cr: 0.03% or more 0.50% or less, B: Any one or more of 0.0003% or more and 0.0050% or less Ti, Nb, V, Zr, Mo, Cr, and B are elements that contribute to an increase in the hardness of the steel sheet. It is preferably contained for imparting hardness. On the other hand, when the content of these elements becomes excessive, the residual stress increases, and flatness after punching or thermal strain occurs.
- Ti content is 0.005% to 0.10%
- Nb content is 0.005% to 0.10%
- V content is 0.005% to 0.50%
- Zr content is 0.005% to 0.10%
- Mo content is It is preferable that the content is 0.02% to 0.50%
- the Cr content is 0.03% to 0.50%
- the B content is 0.0003% to 0.0050%.
- the content is 0.20% or less
- the Cr content is 0.05% or more and 0.20% or less
- the B content is 0.0005% or more and 0.0030% or less.
- Ca 0.0003% or more and 0.0050% or less
- REM 0.0003% or more and 0.0100% or less
- the Ca content is preferably 0.0003% or more and the REM content is preferably 0.0003% or more. More preferably, the Ca content is 0.0008% or more and the REM content is 0.0008% or more.
- the Ca content is preferably 0.0050% or less and the REM content is preferably 0.0100% or less. . More preferably, the Ca content is 0.0030% or less and the REM content is 0.0050% or less.
- any one or more Sb and Sn are elements that improve the surface properties of the steel sheet, and have the effect of improving the adhesion to the friction material. is there.
- the Sb content is preferably 0.001% or more and the Sn content is preferably 0.001% or more.
- the Sb content is preferably 0.030% or less. More preferably, the Sb content is 0.005% or more and 0.020% or less, and the Sn content is 0.005% or more and 0.015% or less.
- the balance other than the above components is Fe and inevitable impurities.
- unavoidable impurities include O, Mg, Co, Zn, Ta, W, Pb, Bi, and the like.
- the content of these elements is acceptable if it is about 0.01% or less.
- the area ratio of the ferrite phase is 80% or more
- the area ratio of the hard phase composed of at least one of the pearlite phase and the bainite phase is 20% or less in total
- the hard phase The average particle size of the hard phase is 1 ⁇ m or more and 10 ⁇ m or less, and the average aspect ratio of the hard phase is 10.0 or less.
- the residual stress of the cold-rolled steel sheet is reduced by making the deformation in the steel sheet uniform during cold rolling.
- the cold-rolled steel sheet of the present invention needs to make the main phase a soft ferrite phase and suppress hard pearlite phase and bainite phase.
- a hard phase composed of one or more of pearlite phase and bainite phase is contained in a large amount exceeding 20% in total area ratio, the residual stress after cold rolling increases, and the steel plate shape after punching Deteriorates, or cracks occur at the interface between the ferrite phase and the hard phase during punching, and the punched end face properties of the steel sheet deteriorate.
- thermal strain characteristics deteriorate as the residual stress increases, thermal strain occurs when such a cold-rolled steel sheet is punched and exposed to a high temperature environment.
- the area ratio of the ferrite phase needs to be 80% or more, and the area ratio of the hard phase composed of at least one of the pearlite phase and the bainite phase needs to be 20% or less in total.
- the area ratio of the ferrite phase is preferably 85% or more, and more preferably 90% or more.
- the total area ratio of the hard phase is preferably 15% or less, and more preferably 10% or less.
- the cold-rolled steel sheet structure of the present invention may contain cementite in addition to the ferrite phase, pearlite phase, and bainite phase.
- the area ratio of cementite is preferably 1% or less.
- the cold-rolled steel sheet of the present invention has a structure in which an average particle diameter of a hard phase composed of at least one of a pearlite phase and a bainite phase is 1 ⁇ m or more and 10 ⁇ m or less, and an average aspect ratio of the hard phase is 10.0 or less.
- an average particle diameter of a hard phase composed of at least one of a pearlite phase and a bainite phase is 1 ⁇ m or more and 10 ⁇ m or less
- an average aspect ratio of the hard phase is 10.0 or less.
- the average particle diameter of the hard phase is 10 ⁇ m or less. Preferably, it is 7 ⁇ m or less.
- the smaller the average particle size of the hard phase the more preferable from the viewpoint of the punchability of the steel sheet.
- it is necessary to lower the finish rolling end temperature and the winding temperature of hot rolling during the production of the steel sheet.
- the finish rolling end temperature and the coiling temperature of hot rolling it is necessary to set the finish rolling end temperature and the coiling temperature of hot rolling to a predetermined temperature or more as described later.
- the average particle size of the hard phase is 1 ⁇ m or more.
- the average aspect ratio of the hard phase exceeds 10.0, the strain at the interface between the hard phase and the ferrite phase, which is the main phase, increases and the residual stress increases, so the heat-resistant strain characteristics of the cold-rolled steel sheet deteriorate. Therefore, the average aspect ratio of the hard phase is 10.0 or less. Preferably it is 8.0 or less.
- the hardness of the cold-rolled steel sheet of the present invention is 170 or more in terms of Hv (Vickers hardness).
- Hv Vehicle hardness
- the hardness of a cold-rolled steel sheet shall be Hv170 or more.
- it is Hv 190 or more.
- the hardness of the cold-rolled steel sheet of the present invention is mainly based on work hardening by cold rolling, if the hardness becomes too high (that is, if the rolling reduction of cold rolling becomes too high). The residual stress of the steel sheet also increases, and the thermal strain characteristics deteriorate. For this reason, it is preferable that the cold-rolled steel sheet has a hardness of Hv250 or less.
- the cold-rolled steel sheet of the present invention is a hot-rolled sheet having a ferrite phase as a main phase by subjecting a steel material having the above chemical composition to hot rolling, and the scale is removed from the hot-rolled sheet by pickling. Thereafter, it is obtained by cold rolling at a predetermined rolling reduction.
- the manufacturing method of the steel material need not be particularly limited.
- molten steel having the above-described composition is melted in a converter or electric furnace, preferably subjected to secondary smelting in a vacuum degassing furnace (vacuum degassing furnace), and slab is obtained by a production method such as continuous casting.
- a vacuum degassing furnace vacuum degassing furnace
- Any conventional method using steel materials such as can be applied.
- the steel material is then subjected to hot rolling consisting of rough rolling and finish rolling to form a hot rolled sheet.
- hot rolling consisting of rough rolling and finish rolling to form a hot rolled sheet.
- the steel material may be subjected to direct rolling (direct rolling) in which hot rolling is performed immediately after casting or after heating for heat supplement after casting.
- the heating temperature is not particularly limited, but is preferably in the range of 1000 ° C. or higher and 1300 ° C. or lower. When the heating temperature is less than 1000 ° C., the deformation resistance becomes high and a good shape may not be obtained. On the other hand, when the temperature is higher than 1300 ° C., scale growth is promoted, and the surface properties of the steel sheet may be deteriorated.
- the conditions for rough rolling are not particularly limited.
- Finish rolling end temperature 800 ° C. or higher and 950 ° C. or lower
- the finish rolling end temperature exceeds 950 ° C.
- the structure of the hot rolled sheet becomes coarse.
- the finish rolling finish temperature is less than 800 ° C.
- the structure of the hot-rolled sheet becomes a structure composed of extremely stretched crystal grains, and the aspect ratio of the hard phase also increases. In this way, when the steel sheet including the hard phase that has been extended in the rolling direction at the stage of hot rolling is further cold-rolled, there is a large difference in hardness between the hard phase and the ferrite phase that is the main phase.
- the finish rolling end temperature is set to 800 ° C. or more and 950 ° C. or less. Preferably they are 850 degreeC or more and 920 degrees C or less.
- Winding temperature More than 600 ° C. and 750 ° C. or less
- the winding temperature is 600 ° C. or less
- a pearlite phase or a bainite phase is excessively formed, and the target steel structure of the ferrite phase cannot be obtained.
- the coiling temperature exceeds 750 ° C.
- the pearlite phase and cementite particles are coarsened to deteriorate the punched end surface properties of the steel plate or the surface properties of the steel plate. Therefore, the coiling temperature is set to more than 600 ° C. and 750 ° C. or less.
- they are 620 degreeC or more and 700 degrees C or less.
- the average cooling rate in the temperature range up to the coiling temperature is preferably 10 ° C./s or more and less than 120 ° C./s. More preferably, it is 15 ° C./s or more and 50 ° C./s or less.
- Cold rolling reduction ratio 30% or more and 70% or less
- the rolling reduction needs to be 30% or more.
- the rolling reduction exceeds 70%, the residual stress increases, the average aspect ratio of the hard phase composed of pearlite and / or bainite phase exceeds a predetermined value, and thermal strain is likely to occur. Therefore, the rolling reduction of cold rolling is set to 30% or more and 70% or less. Preferably they are 40% or more and 60% or less.
- temper rolling may be applied, or a leveler may be passed.
- the elongation rate is preferably 0.3% or more. More preferably, it is 0.4% or more.
- the flatness of the steel sheet after temper rolling it is preferably 1.0% or less.
- test piece is collected, and the structure is observed by the following method.
- the area ratio of the ferrite phase, the pearlite phase, the bainite phase, and the average grain of the hard phase (pearlite phase and / or bainite phase) were determined. Further, test pieces were collected from the obtained cold-rolled steel sheets, and the hardness, flatness after punching, punched end face properties, and heat distortion characteristics were evaluated by the following methods.
- Microstructure observation A sample with a plate thickness cross section parallel to the rolling direction was taken, and the structure was revealed with a 3% nital solution (nital) for the plate thickness cross section, and a scanning electron microscope was used at the 1/4 thickness position. (SEM) was used to photograph 3 fields of view at 500 times, and the area ratio of each phase and the particle size and aspect ratio of the hard phase composed of at least one of pearlite and bainite phases were quantified by image processing.
- the grain size is a square root ( ⁇ (a ⁇ b)) of a value obtained by multiplying the major axis length a and minor axis length b of the crystal grains.
- the aspect ratio is a value (a / b) obtained by dividing the major axis length a of the crystal grains by the minor axis length b.
- the average grain size and average aspect ratio of the hard phase are the arithmetic average of the grain sizes and aspect ratios of all crystal grains recognized as either a pearlite phase or a bainite phase in image processing.
- Hardness Take a sample with a plate thickness cross section parallel to the rolling direction, embed it in a resin, polish the plate thickness cross section, and then use a Vickers hardness tester in accordance with the provisions of JIS Z 2244 at a thickness of 1/4. Used, 5 points were measured with a load of 500 gf, and the average value was determined to be hardness.
- Punched end face properties From the obtained cold-rolled steel sheet, a ring-shaped plate with an outer diameter of 100 mm and an inner diameter of 80 mm is punched, the punched end surfaces are observed, and those without cracks or secondary shear surfaces are punched. : It was set as favorable ((circle)). On the other hand, a punched end surface property: defective (x) was observed where cracks or secondary shear surfaces were observed.
- Heat-resistant strain characteristics A ring-shaped plate having an outer diameter of 100 mm and an inner diameter of 80 mm was punched out from the obtained cold-rolled steel sheet, and the plate was held at 300 ° C. for 1 hour, and then heat-treated by air cooling to room temperature. After the heat treatment, the shape of the plate was measured with a laser measuring instrument in the same manner as in the above “measurement of flatness after punching”, and the difference between the minimum value and the maximum value of the height of the annular portion of the plate was calculated. The case where the difference between the minimum value and the maximum value was 0.2 mm or less was regarded as the heat distortion resistance: good ( ⁇ ). On the other hand, the case where the difference between the minimum value and the maximum value was more than 0.2 mm was regarded as the thermal strain characteristic: defective (x). These results are shown in Table 3.
- each of the cold-rolled steel sheets of the invention examples has a sufficient Vickers hardness of Hv170 or more, excellent flatness after punching, punched end face properties, and excellent thermal strain characteristics.
- the cold-rolled steel sheet of the comparative example outside the scope of the present invention is inferior in any of the characteristics.
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Abstract
Description
例えば、特許文献1では、質量%で、C:0.05~0.6%、Si:2.0%以下、Mn:0.2~2.0%、P:0.03%以下、S:0.03%以下、Sol.Al:0.1%以下、N:0.01%以下を含有し、残部Fe及び不可避不純物からなる鋼を、仕上温度 (Ar3変態点-20℃)以上で熱間圧延した後、冷却速度120℃/秒超、冷却停止温度650℃以下、鋼板幅方向のセンター部とエッジ部との冷却停止温度の差が30℃以下となるように冷却を行い、巻取温度600℃以下で巻取り、酸洗後、圧下率40%以上で冷間圧延するか、もしくは、焼鈍温度600℃以上AC1変態点以下で焼鈍後に圧下率40%以上で冷間圧延することにより、鋼板の板面硬度(surface hardness of steel sheet) Hvが170~300であり、鋼板の長手方向及び幅方向の各位置における板面硬度差の最大値ΔHvが20以下である薄鋼板を製造する技術が提案されている。特許文献1で提案された技術によると、鋼板の長手方向及び幅方向の位置による残留応力の差異が抑制され、打ち抜き後の平坦度(flatness)に優れる冷間圧延ままの薄鋼板が得られるとされている。 Various technologies have been proposed so far for cold-rolled steel sheets for plates and other drive train components.
For example, in Patent Document 1, in mass%, C: 0.05 to 0.6%, Si: 2.0% or less, Mn: 0.2 to 2.0%, P: 0.03% or less, S: 0.03% or less, Sol.Al: 0.1% or less , N: Steel containing less than 0.01%, balance Fe and inevitable impurities, hot-rolled at a finish temperature (Ar 3 transformation point –20 ° C) or higher, cooling rate over 120 ° C / second, cooling stop temperature Cooling is performed so that the difference in cooling stop temperature between the center part and the edge part in the width direction of the steel sheet is 650 ° C or lower, and the cooling temperature is 30 ° C or lower. By cold rolling at the above, or by cold rolling at an annealing temperature of 600 ° C. or more and an AC1 transformation point or less and then rolling at a reduction rate of 40% or more, the surface hardness of the steel sheet Hv is reduced. A technique for manufacturing a thin steel sheet having a maximum hardness difference ΔHv of 20 or less at each position in the longitudinal direction and the width direction of the steel sheet between 170 and 300 has been proposed. According to the technique proposed in Patent Document 1, the difference in residual stress depending on the position in the longitudinal direction and width direction of the steel sheet is suppressed, and a cold-rolled thin steel sheet having excellent flatness after punching is obtained. Has been.
[1] 質量%で、C :0.01%以上0.08%以下、Si:0.01%以上1.0%以下、Mn:0.05%以上1.0%以下、P :0.03%以下、S :0.015%以下、Al:0.005%以上0.10%以下、N :0.01%以下を含有し、残部がFeおよび不可避的不純物からなる組成と、フェライト相の面積率が80%以上であり、パーライト相、ベイナイト相のいずれか1種以上からなる硬質相の面積率が合計で20%以下であり、前記硬質相の平均粒径が1μm以上10μm以下、かつ、前記硬質相の平均アスペクト比が10.0以下である組織とを有し、ビッカース硬さ(Vickers hardness)がHv170以上である、打ち抜き性および耐熱ひずみ特性に優れた冷延鋼板。 The present invention has been completed based on the above findings, and the gist of the present invention is as follows.
[1] By mass%, C: 0.01% to 0.08%, Si: 0.01% to 1.0%, Mn: 0.05% to 1.0%, P: 0.03% or less, S: 0.015% or less, Al: 0.005% 0.10% or less, N: 0.01% or less, with the balance consisting of Fe and inevitable impurities, the area ratio of the ferrite phase is 80% or more, and from one or more of pearlite phase and bainite phase The hard phase has a total area ratio of 20% or less, an average particle size of the hard phase of 1 μm to 10 μm, and an average aspect ratio of the hard phase of 10.0 or less, and a Vickers hard A cold-rolled steel sheet having a Vickers hardness of Hv170 or more and excellent in punchability and thermal strain characteristics.
Cは、鋼板の強化に必要な元素であり、プレートやディスクなどの駆動系部品用素材として必要な硬さを得るためには、C含有量を0.01%以上とする必要がある。一方、C含有量が0.08%を超えると、硬さが過剰に高くなり、また、パーライト分率が上昇して、打ち抜き後の平坦度が劣化するとともに、打ち抜き端面性状が劣化する。したがって、C含有量の上限を0.08%とする。特に打ち抜き端面性状の観点からは、C含有量を0.05%未満とすることが好ましい。より好ましくは、0.04%以下である。 C: 0.01% or more and 0.08% or less C is an element necessary for strengthening steel sheets. To obtain the hardness required for drive system parts such as plates and disks, the C content is 0.01% or more. There is a need to. On the other hand, if the C content exceeds 0.08%, the hardness becomes excessively high, the pearlite fraction increases, the flatness after punching deteriorates, and the punched end face properties deteriorate. Therefore, the upper limit of C content is 0.08%. In particular, from the viewpoint of punched end face properties, the C content is preferably less than 0.05%. More preferably, it is 0.04% or less.
Siは、鋼の脱酸剤(deoxidizer)であり、鋼の清浄度(cleanliness)を向上させる効果があるため、含有量を0.01%以上とする。Siは、固溶強化(solid solution hardening)により鋼板の硬さを上昇させる元素でもあり、所望の硬さを得るために添加することができる。但し、Si含有量が1.0%を超えると、鋼板の表面性状(surface quality)が劣化するため、Si含有量の上限を1.0%とする。特に摩擦を発生させる部品に使用されるプレート材では良好な表面性状が要求されるため、0.6%以下とすることが好ましい。 Si: 0.01% or more and 1.0% or less Si is a deoxidizer for steel and has the effect of improving the cleanliness of the steel, so the content is made 0.01% or more. Si is also an element that increases the hardness of the steel sheet by solid solution hardening, and can be added to obtain a desired hardness. However, if the Si content exceeds 1.0%, the surface quality of the steel sheet deteriorates, so the upper limit of the Si content is 1.0%. In particular, a plate material used for a component that generates friction is required to have good surface properties, and therefore, it is preferably set to 0.6% or less.
Mnは、固溶強化により、鋼板の硬さを上昇させる元素であり、所望の硬さを得るためにはMn含有量を0.05%以上とする必要がある。好ましくは0.1%以上である。Mn含有量が1.0%を超えると、パーライトやベイナイトなどが過剰に生成することに加え、偏析(segregation)によりパーライト等が層状に生成して、打ち抜き端面性状が劣化する。したがって、Mn含有量は1.0%以下とする。好ましくは0.5%以下である。 Mn: 0.05% or more and 1.0% or less Mn is an element that increases the hardness of the steel sheet by solid solution strengthening, and the Mn content needs to be 0.05% or more in order to obtain a desired hardness. Preferably it is 0.1% or more. If the Mn content exceeds 1.0%, in addition to excessive generation of pearlite, bainite, etc., pearlite and the like are generated in layers due to segregation, and the punched end face properties deteriorate. Therefore, the Mn content is 1.0% or less. Preferably it is 0.5% or less.
Pは、鋼中で偏析し易い元素であり、多量に含有するとPの偏析により層状組織の形成が促進され、打ち抜き端面性状が劣化する。したがって、P含有量は0.03%以下とする必要がある。好ましくは0.02%以下である。 P: 0.03% or less P is an element that is easily segregated in steel. When it is contained in a large amount, the formation of a layered structure is promoted by the segregation of P, and the punched end face properties deteriorate. Therefore, the P content needs to be 0.03% or less. Preferably it is 0.02% or less.
Sは、MnS等の硫化物系介在物を形成し、打ち抜き端面性状を劣化させる。したがって、S含有量は0.015%以下とする必要がある。好ましくは0.010%以下である。 S: 0.015% or less S forms sulfide inclusions such as MnS and degrades the punched end face properties. Therefore, the S content needs to be 0.015% or less. Preferably it is 0.010% or less.
Alは、脱酸元素として添加することにより、鋼板の清浄度を向上させることができるため、その含有量を0.005%以上とする必要がある。好ましくは0.03%以上である。一方、Al含有量が0.10%を超えると、酸化物が過剰に生成して表面性状が劣化し、摩擦材との接着性が劣化する。したがって、Al含有量は0.10%以下とする。好ましくは0.08%以下である。 Al: 0.005% or more and 0.10% or less Since Al can improve the cleanliness of the steel sheet by adding it as a deoxidizing element, its content needs to be 0.005% or more. Preferably it is 0.03% or more. On the other hand, if the Al content exceeds 0.10%, oxides are excessively generated, the surface properties are deteriorated, and the adhesion to the friction material is deteriorated. Therefore, the Al content is 0.10% or less. Preferably it is 0.08% or less.
Nは、本発明において有害な元素であり、その含有量が過剰になると鋼板の延性が低下し、打ち抜き端面性状が劣化する。したがって、N含有量は0.01%以下とする。好ましくは0.006%以下である。 N: 0.01% or less N is a harmful element in the present invention, and if its content is excessive, the ductility of the steel sheet is lowered and the punched end face properties are deteriorated. Therefore, the N content is 0.01% or less. Preferably it is 0.006% or less.
CuおよびNiは、固溶強化により鋼板の硬さの上昇に寄与する元素であり、鋼板に所望の硬さを付与するために含有することができる。このような効果を得るためには、Cu含有量を0.01%以上、Ni含有量を0.01%以上とすることが好ましい。Cu含有量は0.02%以上、Ni含有量は0.02%以上とすることがより好ましい。一方、これらの元素の含有量が過剰になると、表面性状が劣化し、摩擦材との接着性が劣化する。したがって、Cu含有量は0.20%以下、Ni含有量は0.50%以下とすることが好ましい。Cu含有量は0.10%以下、Ni含有量は0.30%以下とすることがより好ましい。 Cu: 0.01% or more and 0.20% or less, Ni: 0.01% or more and 0.50% or less Any one or more of Cu and Ni are elements that contribute to an increase in the hardness of the steel sheet by solid solution strengthening. It can be contained in order to impart a thickness. In order to obtain such an effect, it is preferable that the Cu content is 0.01% or more and the Ni content is 0.01% or more. More preferably, the Cu content is 0.02% or more, and the Ni content is 0.02% or more. On the other hand, when the content of these elements is excessive, the surface properties are deteriorated and the adhesion to the friction material is deteriorated. Therefore, the Cu content is preferably 0.20% or less and the Ni content is preferably 0.50% or less. More preferably, the Cu content is 0.10% or less, and the Ni content is 0.30% or less.
Ti、Nb、V、Zr、Mo、Cr、Bは、鋼板の硬さの上昇に寄与する元素であり、鋼板に所望の硬さを付与するために含有することが好ましい。一方、これらの元素の含有量が過剰になると、残留応力が大きくなり、打ち抜き後の平坦度や、熱ひずみが発生する。したがって、Ti含有量は0.005%以上0.10%以下、Nb含有量は0.005%以上0.10%以下、V 含有量は0.005%以上0.50%以下、Zr含有量は0.005%以上0.10%以下、Mo含有量は0.02%以上0.50%以下、Cr含有量は0.03%以上0.50%以下、B含有量は0.0003%以上0.0050%以下とすることが好ましい。Ti含有量は0.008%以上0.03%以下、Nb含有量は0.008%以上0.05%以下、V含有量は0.01%以上0.20%以下、Zr含有量は0.01%以上0.03%以下、Mo含有量は0.05%以上0.20%以下、Cr含有量は0.05%以上0.20%以下、B含有量は0.0005%以上0.0030%以下とすることがより好ましい。 Ti: 0.005% to 0.10%, Nb: 0.005% to 0.10%, V: 0.005% to 0.50%, Zr: 0.005% to 0.10%, Mo: 0.02% to 0.50%, Cr: 0.03% or more 0.50% or less, B: Any one or more of 0.0003% or more and 0.0050% or less Ti, Nb, V, Zr, Mo, Cr, and B are elements that contribute to an increase in the hardness of the steel sheet. It is preferably contained for imparting hardness. On the other hand, when the content of these elements becomes excessive, the residual stress increases, and flatness after punching or thermal strain occurs. Therefore, Ti content is 0.005% to 0.10%, Nb content is 0.005% to 0.10%, V content is 0.005% to 0.50%, Zr content is 0.005% to 0.10%, Mo content is It is preferable that the content is 0.02% to 0.50%, the Cr content is 0.03% to 0.50%, and the B content is 0.0003% to 0.0050%. Ti content 0.008% to 0.03%, Nb content 0.008% to 0.05%, V content 0.01% to 0.20%, Zr content 0.01% to 0.03%, Mo content 0.05% More preferably, the content is 0.20% or less, the Cr content is 0.05% or more and 0.20% or less, and the B content is 0.0005% or more and 0.0030% or less.
Ca、REMはいずれも、硫化物の形態を球状に制御し、鋼板の打ち抜き端面性状を向上させる作用を有する元素であり、必要に応じて含有できる。このような効果を得るためには、Ca含有量を0.0003%以上、REM含有量を0.0003%以上とすることが好ましい。Ca含有量を0.0008%以上、REM含有量を0.0008%以上とすることがより好ましい。一方、これらの元素の含有量が過剰になると、介在物が増大して、鋼板の打ち抜き端面性状を劣化させるため、Ca含有量を0.0050%以下、REM含有量を0.0100%以下とすることが好ましい。また、Ca含有量を0.0030%以下、REM含有量を0.0050%以下とすることがより好ましい。 Ca: 0.0003% or more and 0.0050% or less, REM: 0.0003% or more and 0.0100% or less One or more of Ca and REM both control the shape of the sulfide to be spherical and improve the punched end face properties of the steel sheet. It can be contained if necessary. In order to obtain such effects, the Ca content is preferably 0.0003% or more and the REM content is preferably 0.0003% or more. More preferably, the Ca content is 0.0008% or more and the REM content is 0.0008% or more. On the other hand, when the content of these elements becomes excessive, inclusions increase and the punched end face properties of the steel sheet are deteriorated. Therefore, the Ca content is preferably 0.0050% or less and the REM content is preferably 0.0100% or less. . More preferably, the Ca content is 0.0030% or less and the REM content is 0.0050% or less.
SbおよびSnは、鋼板の表面性状を向上させる元素であり、摩擦材との接着性を向上させる効果がある。このような効果を得るためには、Sb含有量を0.001%以上、Sn含有量を0.001%以上とすることが好ましい。一方、これらの元素の含有量が過剰になると、表面偏析(surface segregation)が顕著になり、鋼板の表面性状が劣化して摩擦材との接着性が低下するため、Sb含有量を0.030%以下、Sn含有量を0.030%以下とすることが好ましい。Sb含有量を0.005%以上0.020%以下、Sn含有量を0.005%以上0.015%以下とすることがより好ましい。 Sb: 0.001% or more and 0.030% or less, Sn: 0.001% or more and 0.030% or less, any one or more Sb and Sn are elements that improve the surface properties of the steel sheet, and have the effect of improving the adhesion to the friction material. is there. In order to obtain such an effect, the Sb content is preferably 0.001% or more and the Sn content is preferably 0.001% or more. On the other hand, if the content of these elements is excessive, surface segregation becomes prominent, the surface properties of the steel sheet deteriorate and the adhesion to the friction material decreases, so the Sb content is 0.030% or less. The Sn content is preferably 0.030% or less. More preferably, the Sb content is 0.005% or more and 0.020% or less, and the Sn content is 0.005% or more and 0.015% or less.
本発明の冷延鋼板は、フェライト相の面積率が80%以上であり、パーライト相、ベイナイト相のいずれか1種以上からなる硬質相の面積率が合計で20%以下であり、前記硬質相の平均粒径が1μm以上10μm以下、かつ、前記硬質相の平均アスペクト比が10.0以下である組織を有する。 Next, the structure of the cold-rolled steel sheet of the present invention will be described.
In the cold-rolled steel sheet of the present invention, the area ratio of the ferrite phase is 80% or more, the area ratio of the hard phase composed of at least one of the pearlite phase and the bainite phase is 20% or less in total, and the hard phase The average particle size of the hard phase is 1 μm or more and 10 μm or less, and the average aspect ratio of the hard phase is 10.0 or less.
本発明の冷延鋼板は、前記の化学組成を有する鋼素材に熱間圧延を施して、フェライト相を主相とする熱延板とし、この熱延板を、酸洗にてスケールを除去した後、所定の圧下率で冷間圧延することによって得られる。 Next, the manufacturing method of the cold rolled steel sheet of this invention is demonstrated.
The cold-rolled steel sheet of the present invention is a hot-rolled sheet having a ferrite phase as a main phase by subjecting a steel material having the above chemical composition to hot rolling, and the scale is removed from the hot-rolled sheet by pickling. Thereafter, it is obtained by cold rolling at a predetermined rolling reduction.
仕上げ圧延終了温度が950℃を超えると、熱延板の組織が粗大化する。その結果、冷間圧延後の鋼板の硬質相の平均粒径が大きくなるため、打ち抜き端面性状が劣化する。一方、仕上げ圧延終了温度が800℃未満では、熱延板の組織が極端に伸展した結晶粒からなる組織となり、硬質相のアスペクト比も大きくなる。このように熱延板の段階で圧延方向に伸展した硬質相を含む鋼板を更に冷間圧延すると、硬質相と主相であるフェライト相との硬度差が大きいため、圧延方向に組織が伸長する際に硬質相と主相であるフェライト相との界面に大きな残留応力が発生する。このため、冷間圧延後の鋼板に蓄積される残留応力が大きくなり、熱ひずみが発生し易くなる。したがって、仕上げ圧延終了温度は800℃以上950℃以下とする。好ましくは850℃以上920℃以下である。 Finish rolling end temperature: 800 ° C. or higher and 950 ° C. or lower When the finish rolling end temperature exceeds 950 ° C., the structure of the hot rolled sheet becomes coarse. As a result, since the average grain size of the hard phase of the steel sheet after cold rolling becomes large, the punched end face properties deteriorate. On the other hand, when the finish rolling finish temperature is less than 800 ° C., the structure of the hot-rolled sheet becomes a structure composed of extremely stretched crystal grains, and the aspect ratio of the hard phase also increases. In this way, when the steel sheet including the hard phase that has been extended in the rolling direction at the stage of hot rolling is further cold-rolled, there is a large difference in hardness between the hard phase and the ferrite phase that is the main phase. At the same time, a large residual stress is generated at the interface between the hard phase and the ferrite phase as the main phase. For this reason, the residual stress accumulate | stored in the steel plate after cold rolling becomes large, and it becomes easy to generate | occur | produce a thermal strain. Therefore, the finish rolling end temperature is set to 800 ° C. or more and 950 ° C. or less. Preferably they are 850 degreeC or more and 920 degrees C or less.
巻取り温度が600℃以下では、パーライト相やベイナイト相が過剰に生成して、目的とするフェライト相主体の鋼板組織が得られない。一方、巻取り温度が750℃を超えると、パーライト相やセメンタイト粒子が粗大化して鋼板の打ち抜き端面性状が劣化したり、鋼板の表面性状が劣化する。したがって、巻取り温度を600℃超750℃以下とする。好ましくは620℃以上700℃以下である。 Winding temperature: More than 600 ° C. and 750 ° C. or less When the winding temperature is 600 ° C. or less, a pearlite phase or a bainite phase is excessively formed, and the target steel structure of the ferrite phase cannot be obtained. On the other hand, when the coiling temperature exceeds 750 ° C., the pearlite phase and cementite particles are coarsened to deteriorate the punched end surface properties of the steel plate or the surface properties of the steel plate. Therefore, the coiling temperature is set to more than 600 ° C. and 750 ° C. or less. Preferably they are 620 degreeC or more and 700 degrees C or less.
以上のようにして得られた熱延板は、酸洗にてスケールを除去したのち、冷間圧延を施して冷延鋼板とされる。 Although there is no particular limitation on the cooling rate when cooling to the coiling temperature after the finish rolling is finished, in order to obtain the desired structure of the hot-rolled sheet and the finally obtained cold-rolled sheet, from the finish rolling end temperature. The average cooling rate in the temperature range up to the coiling temperature is preferably 10 ° C./s or more and less than 120 ° C./s. More preferably, it is 15 ° C./s or more and 50 ° C./s or less.
The hot-rolled sheet obtained as described above is removed from the scale by pickling and then cold-rolled to obtain a cold-rolled steel sheet.
冷間圧延によりプレートなどの駆動系部品用素材として必要な鋼板硬さとするためには、圧下率を30%以上とする必要がある。一方、圧下率が70%を超えると、残留応力が大きくなり、パーライトおよび/またはベイナイト相からなる硬質相の平均アスペクト比が所定の値を超え、熱ひずみが発生し易くなる。したがって、冷間圧延の圧下率を30%以上70%以下とする。好ましくは40%以上60%以下である。 Cold rolling reduction ratio: 30% or more and 70% or less In order to obtain a steel sheet hardness necessary for a material for a drive system component such as a plate by cold rolling, the rolling reduction needs to be 30% or more. On the other hand, when the rolling reduction exceeds 70%, the residual stress increases, the average aspect ratio of the hard phase composed of pearlite and / or bainite phase exceeds a predetermined value, and thermal strain is likely to occur. Therefore, the rolling reduction of cold rolling is set to 30% or more and 70% or less. Preferably they are 40% or more and 60% or less.
圧延方向に平行な板厚断面の試料を採取し、板厚断面について3%ナイタール溶液(nital)で組織を現出して、板厚1/4位置にて走査電子顕微鏡(scanning electron microscope)(SEM)を用い500倍で3視野撮影し、画像処理により各相の面積率、および、パーライト、ベイナイト相のいずれか1種以上からなる硬質相の粒径とアスペクト比を定量化した。粒径は、結晶粒の長軸長さaと短軸長さbを乗じた値の平方根(√(a×b))とする。アスペクト比は、結晶粒の長軸長さaを短軸長さbで除した値(a/b)とする。硬質相の平均粒径および平均アスペクト比は、画像処理において、パーライト相或いはベイナイト相のいずれかと認識された全ての結晶粒の粒径、アスペクト比の算術平均である。 Microstructure observation A sample with a plate thickness cross section parallel to the rolling direction was taken, and the structure was revealed with a 3% nital solution (nital) for the plate thickness cross section, and a scanning electron microscope was used at the 1/4 thickness position. (SEM) was used to photograph 3 fields of view at 500 times, and the area ratio of each phase and the particle size and aspect ratio of the hard phase composed of at least one of pearlite and bainite phases were quantified by image processing. The grain size is a square root (√ (a × b)) of a value obtained by multiplying the major axis length a and minor axis length b of the crystal grains. The aspect ratio is a value (a / b) obtained by dividing the major axis length a of the crystal grains by the minor axis length b. The average grain size and average aspect ratio of the hard phase are the arithmetic average of the grain sizes and aspect ratios of all crystal grains recognized as either a pearlite phase or a bainite phase in image processing.
圧延方向に平行な板厚断面の試料を採取し、樹脂に埋め込み、板厚断面を研磨後、板厚1/4の位置にて、JIS Z 2244の規定に準拠してビッカース硬度計を用い、荷重500gfで5点測定し、その平均値を硬さとした。 Hardness Take a sample with a plate thickness cross section parallel to the rolling direction, embed it in a resin, polish the plate thickness cross section, and then use a Vickers hardness tester in accordance with the provisions of JIS Z 2244 at a thickness of 1/4. Used, 5 points were measured with a load of 500 gf, and the average value was determined to be hardness.
得られた冷延鋼板から、外径100mm、内径80 mmのリング状のプレートを打ち抜き、
レーザー測定器(laser displacement meter)の測定テーブル上にプレートを置き、レーザー測定器によりテーブルからプレートの円環部上面までの高さを円環部全体について測定し、その最小値と最大値の差を算出した。最小値と最大値の差が0.2 mm以下である場合を平坦度:良好(○)とした。一方、最小値と最大値の差が0.2mm超である場合を平坦度:不良(×)とした。 Flatness after punching From the obtained cold-rolled steel sheet, a ring-shaped plate with an outer diameter of 100 mm and an inner diameter of 80 mm is punched,
Place the plate on the measurement table of the laser displacement meter, measure the height from the table to the top surface of the annular portion of the plate with the laser measurement device, and check the difference between the minimum and maximum values. Was calculated. When the difference between the minimum value and the maximum value is 0.2 mm or less, the flatness: good (◯). On the other hand, the case where the difference between the minimum value and the maximum value was more than 0.2 mm was defined as flatness: defective (x).
得られた冷延鋼板から、外径100mm、内径80 mmのリング状のプレートを打ち抜き、打ち抜き端面を観察し、ワレや2次せん断面(secondary shear surface)のないものを打ち抜き端面性状:良好(○)とした。一方、ワレや2次せん断面が観察されたものを打ち抜き端面性状:不良(×)とした。 Punched end face properties From the obtained cold-rolled steel sheet, a ring-shaped plate with an outer diameter of 100 mm and an inner diameter of 80 mm is punched, the punched end surfaces are observed, and those without cracks or secondary shear surfaces are punched. : It was set as favorable ((circle)). On the other hand, a punched end surface property: defective (x) was observed where cracks or secondary shear surfaces were observed.
得られた冷延鋼板から、外径100mm、内径80 mmのリング状のプレートを打ち抜き、プレートを300℃で1hr保持後、室温まで空冷する熱処理を行った。熱処理後、前記「打ち抜き後の平坦度測定」と同様に、レーザー測定器によりプレートの形状を測定し、プレートの円環部の高さの最小値と最大値の差を算出した。
最小値と最大値の差が0.2mm以下である場合を耐熱ひずみ特性:良好(○)とした。一方、最小値と最大値の差が0.2mm超である場合を耐熱ひずみ特性:不良(×)とした。
これらの結果を、表3に示す。 Heat-resistant strain characteristics A ring-shaped plate having an outer diameter of 100 mm and an inner diameter of 80 mm was punched out from the obtained cold-rolled steel sheet, and the plate was held at 300 ° C. for 1 hour, and then heat-treated by air cooling to room temperature. After the heat treatment, the shape of the plate was measured with a laser measuring instrument in the same manner as in the above “measurement of flatness after punching”, and the difference between the minimum value and the maximum value of the height of the annular portion of the plate was calculated.
The case where the difference between the minimum value and the maximum value was 0.2 mm or less was regarded as the heat distortion resistance: good (◯). On the other hand, the case where the difference between the minimum value and the maximum value was more than 0.2 mm was regarded as the thermal strain characteristic: defective (x).
These results are shown in Table 3.
本出願は、2013年4月2日に日本に出願された特願2013-076860号に基づき優先権を主張するものであって、その内容の全てここに取り込む。 Each of the cold-rolled steel sheets of the invention examples has a sufficient Vickers hardness of Hv170 or more, excellent flatness after punching, punched end face properties, and excellent thermal strain characteristics. On the other hand, the cold-rolled steel sheet of the comparative example outside the scope of the present invention is inferior in any of the characteristics.
This application claims priority based on Japanese Patent Application No. 2013-076860 filed in Japan on April 2, 2013, the entire contents of which are incorporated herein.
Claims (11)
- 質量%で、
C :0.01%以上0.08%以下、 Si:0.01%以上1.0%以下、
Mn:0.05%以上1.0%以下、 P :0.03%以下、
S :0.015%以下、 Al:0.005%以上0.10%以下、
N :0.01%以下
を含有し、残部がFeおよび不可避的不純物からなる組成と、フェライト相の面積率が80%以上であり、パーライト相、ベイナイト相のいずれか1種以上からなる硬質相の面積率が合計で20%以下であり、前記硬質相の平均粒径が1μm以上10μm以下、かつ、前記硬質相の平均アスペクト比が10.0以下である組織とを有し、ビッカース硬さがHv170以上である冷延鋼板。 % By mass
C: 0.01% to 0.08%, Si: 0.01% to 1.0%,
Mn: 0.05% or more and 1.0% or less, P: 0.03% or less,
S: 0.015% or less, Al: 0.005% or more and 0.10% or less,
N: A composition containing 0.01% or less, the balance being Fe and inevitable impurities, and the area ratio of the ferrite phase being 80% or more, and the area of the hard phase consisting of at least one of the pearlite phase and the bainite phase The ratio is 20% or less in total, the hard phase has an average particle diameter of 1 μm or more and 10 μm or less, and the hard phase has an average aspect ratio of 10.0 or less, and the Vickers hardness is Hv 170 or more. A cold-rolled steel sheet. - 前記組成に加えて更に、質量%で、Cu:0.01%以上0.20%以下、Ni:0.01%以上0.50%以下のいずれか1種以上を含有する請求項1に記載の冷延鋼板。 The cold-rolled steel sheet according to claim 1, further comprising at least one of Cu: 0.01% to 0.20% and Ni: 0.01% to 0.50% in addition to the composition.
- 前記組成に加えて更に、質量%で、Ti:0.005%以上0.10%以下、Nb:0.005%以上0.10%以下、V:0.005%以上0.50%以下、Zr:0.005%以上0.10%以下、Mo:0.02%以上0.50%以下、Cr:0.03%以上0.50%以下、B:0.0003%以上0.0050%以下のいずれか1種以上を含有する請求項1または2に記載の冷延鋼板。 In addition to the above composition, Ti: 0.005% to 0.10%, Nb: 0.005% to 0.10%, V: 0.005% to 0.50%, Zr: 0.005% to 0.10%, Mo: 0.02 The cold-rolled steel sheet according to claim 1 or 2, comprising at least one of Cr: 0.03% to 0.50%, B: 0.0003% to 0.0050%.
- 前記組成に加えて更に、質量%で、Ca:0.0003%以上0.0050%以下、REM:0.0003%以上0.0100%以下のいずれか1種以上を含有する請求項1ないし3のいずれかに記載の冷延鋼板。 The cold rolling according to any one of claims 1 to 3, further comprising at least one of Ca: 0.0003% to 0.0050% and REM: 0.0003% to 0.0100% in addition to the composition. steel sheet.
- 前記組成に加えて更に、質量%で、Sb:0.001%以上0.030%以下、Sn:0.001%以上0.030%以下のいずれか1種以上を含有する請求項1ないし4のいずれかに記載の冷延鋼板。 The cold rolling according to any one of claims 1 to 4, further comprising at least one of Sb: 0.001% to 0.030% and Sn: 0.001% to 0.030% in addition to the composition. steel sheet.
- 質量%で、
C :0.01%以上0.08%以下、 Si:0.01%以上1.0%以下、
Mn:0.05%以上1.0%以下、 P :0.03%以下、
S :0.015%以下、 Al:0.005%以上0.10%以下、
N :0.01%以下
を含有し、残部がFeおよび不可避的不純物からなる組成を有する鋼素材に、仕上げ圧延終了温度を800℃以上950℃以下とする熱間圧延を施し、熱間圧延終了後、600℃超750℃以下の巻取り温度で巻き取り、酸洗にてスケールを除去したのち、30%以上70%以下の圧下率で冷間圧延を施す冷延鋼板の製造方法。 % By mass
C: 0.01% to 0.08%, Si: 0.01% to 1.0%,
Mn: 0.05% or more and 1.0% or less, P: 0.03% or less,
S: 0.015% or less, Al: 0.005% or more and 0.10% or less,
N: A steel material containing 0.01% or less and the balance of Fe and inevitable impurities is subjected to hot rolling with a finish rolling finish temperature of 800 ° C. or more and 950 ° C. or less, and after hot rolling is finished, A method for producing a cold-rolled steel sheet, which is wound at a coiling temperature of 600 ° C. or higher and 750 ° C. or lower, removed the scale by pickling, and then cold-rolled at a rolling reduction of 30% to 70%. - 前記冷間圧延を施したのち、調質圧延を施す請求項6に記載の冷延鋼板の製造方法。 The method for producing a cold-rolled steel sheet according to claim 6, wherein after the cold rolling, temper rolling is performed.
- 前記組成に加えて更に、質量%で、Cu:0.01%以上0.20%以下、Ni:0.01%以上0.50%以下のいずれか1種以上を含有する請求項6または7に記載の冷延鋼板の製造方法。 The manufacturing of the cold-rolled steel sheet according to claim 6 or 7, further comprising at least one of Cu: 0.01% to 0.20% and Ni: 0.01% to 0.50% in addition to the composition. Method.
- 前記組成に加えて更に、質量%で、Ti:0.005%以上0.10%以下、Nb:0.005%以上0.10%以下、V:0.005%以上0.50%以下、Zr:0.005%以上0.10%以下、Mo:0.02%以上0.50%以下、Cr:0.03%以上0.50%以下、B:0.0003%以上0.0050%以下のいずれか1種以上を含有する請求項6ないし8のいずれかに記載の冷延鋼板の製造方法。 In addition to the above composition, Ti: 0.005% to 0.10%, Nb: 0.005% to 0.10%, V: 0.005% to 0.50%, Zr: 0.005% to 0.10%, Mo: 0.02 % Or more and 0.50% or less, Cr: 0.03% or more and 0.50% or less, B: 0.0003% or more and 0.0050% or less, The manufacturing method of the cold-rolled steel plate in any one of Claim 6 thru | or 8.
- 前記組成に加えて更に、質量%で、Ca:0.0003%以上0.0050%以下、REM:0.0003%以上0.0100%以下のいずれか1種以上を含有する請求項6ないし9のいずれかに記載の冷延鋼板の製造方法。 The cold rolling according to any one of claims 6 to 9, further comprising at least one of Ca: 0.0003% to 0.0050% and REM: 0.0003% to 0.0100% in addition to the composition. A method of manufacturing a steel sheet.
- 前記組成に加えて更に、質量%で、Sb:0.001%以上0.030%以下、Sn:0.001%以上0.030%以下のいずれか1種以上を含有する請求項6ないし10のいずれかに記載の冷延鋼板の製造方法。 The cold rolling according to any one of claims 6 to 10, further comprising at least one of Sb: 0.001% to 0.030% and Sn: 0.001% to 0.030% in addition to the composition. A method of manufacturing a steel sheet.
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- 2014-03-07 KR KR1020157024635A patent/KR101717002B1/en active IP Right Grant
- 2014-03-07 CN CN201480019854.2A patent/CN105074039B/en active Active
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EP3257959A4 (en) * | 2015-03-27 | 2017-12-20 | JFE Steel Corporation | High-strength steel sheet and production method therefor |
US10570476B2 (en) | 2015-03-27 | 2020-02-25 | Jfe Steel Corporation | High-strength steel sheet and production method therefor |
EP3584340A4 (en) * | 2017-02-20 | 2020-11-04 | Nippon Steel Corporation | Steel sheet and manufacturing method therefor |
Also Published As
Publication number | Publication date |
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TWI551696B (en) | 2016-10-01 |
MX2015013941A (en) | 2015-12-08 |
TW201441383A (en) | 2014-11-01 |
TW201621061A (en) | 2016-06-16 |
KR20150119097A (en) | 2015-10-23 |
KR101717002B1 (en) | 2017-03-15 |
TWI534273B (en) | 2016-05-21 |
JP5633594B2 (en) | 2014-12-03 |
CN105074039A (en) | 2015-11-18 |
JP2014201766A (en) | 2014-10-27 |
CN105074039B (en) | 2017-03-15 |
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