WO2011162135A1 - Cold-rolled thin steel sheet having excellent shape fixability, and process for production thereof - Google Patents

Cold-rolled thin steel sheet having excellent shape fixability, and process for production thereof Download PDF

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WO2011162135A1
WO2011162135A1 PCT/JP2011/063626 JP2011063626W WO2011162135A1 WO 2011162135 A1 WO2011162135 A1 WO 2011162135A1 JP 2011063626 W JP2011063626 W JP 2011063626W WO 2011162135 A1 WO2011162135 A1 WO 2011162135A1
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cold
less
rolled
steel sheet
thin steel
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PCT/JP2011/063626
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French (fr)
Japanese (ja)
Inventor
太郎 木津
英子 安原
藤田　耕一郎
重宏 ▲高▼城
花澤　和浩
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Ｊｆｅスチール株式会社
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Priority to KR1020127033254A priority Critical patent/KR101479391B1/en
Priority to MX2012013968A priority patent/MX336858B/en
Priority to CN201180031182.3A priority patent/CN102947476B/en
Publication of WO2011162135A1 publication Critical patent/WO2011162135A1/en

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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
    • 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
    • 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
    • C21D8/0442—Flattening; Dressing; Flexing
    • 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
    • C21D8/0447—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 heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • 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
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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

Definitions

  • the present invention relates to a cold-rolled thin steel sheet suitable for structural members such as electrical appliances, office equipment, and automobile members, and particularly suitable for members requiring high dimensional accuracy after press forming.
  • the present invention relates to a cold-rolled thin steel sheet having excellent freezing properties.
  • the “thin steel plate” is a steel plate having a thickness of 0.2 to 2.0 mm, and includes a steel plate and a steel strip.
  • Patent Document 1 discloses that the average value of the X-ray random intensity ratio of ⁇ 100 ⁇ ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> orientation group is 3.0 or more and ⁇ 554 ⁇ ⁇ 225>, ⁇ 111 ⁇ ⁇ 112>, ⁇ 111 ⁇ ⁇ 110> Three crystal orientations of X-ray random intensity ratio of the average value of 3.5 or less to develop a texture with a specific orientation, further rolling direction A ferritic thin steel sheet having excellent shape freezing properties, mainly bending, in which at least one of the r value and the r value perpendicular to the rolling direction is 0.7 or less is described. The steel sheet described in Patent Document 1 is markedly improved in bend formability, has a small amount of springback, and is excellent in shape freezing, mainly bending.
  • Patent Document 2 has a structure in which an island-like structure including martensite is dispersed in a ferrite matrix, the surface average roughness Ha is 0.4 to 1.8 ⁇ m, and the PPI value is 80 or more at a 0.5 ⁇ m count level.
  • the object of the present invention is to solve the problems of the prior art and propose a cold-rolled thin steel sheet having excellent shape freezing property and a method for producing the same.
  • the present inventors have intensively studied various factors affecting the shape freezing property.
  • the present inventors consider that the defective shape of the product (member) at the time of press molding is caused by the elastic strain introduced at the time of press molding being released when the product (member) is taken out from the press mold, We focused on the proportional limit of the steel sheet.
  • the proportional limit is the limit of stress that can maintain a proportional relationship with strain when an external force is applied to the elastic body. While the stress is small, Hooke's law holds, so a proportional relationship is seen.
  • Steel plates having various proportional limits were prepared, parts of a predetermined shape were formed by press forming, and the shape freezing property after forming was investigated. As a result, it was found that the proportional limit of the steel plate needs to be reduced to 150 MPa or less in order to ensure the desired excellent shape freezing property.
  • the proportional limit of the steel plate is 150 MPa or less, the increase in the opening amount X is small and excellent shape freezing property can be maintained, but if the proportional limit of the steel plate exceeds 150 MPa and becomes large, the opening amount X Increases rapidly and the shape freezing property is remarkably lowered.
  • the present inventors diligently studied various factors affecting the proportional limit of the steel sheet in order to stably manufacture the steel sheet having the proportional limit described above. As a result, it was found that the proportional limit can be easily reduced by subjecting a steel sheet mainly composed of a ferrite phase having a relatively large crystal grain size to temper rolling using a roll having a small surface roughness. Next, experimental results that serve as a basis for the above-described knowledge will be described.
  • composition of 0.040% C-0.01% Si-0. 20% Mn-0.01% P-0.01% S-0.04% Al-0.003% N-balance Fe in mass% A cold-rolled annealed plate (thickness: 0.8 mm) having a structure composed of a ferrite single phase with an average crystal grain size of 10 ⁇ m was subjected to temper rolling with a rolling elongation of 1%. In temper rolling, various rolling rolls having a surface roughness Ra adjusted to 0.2 to 2.5 ⁇ m were used. A JIS No. 5 test piece was taken from each temper-rolled steel sheet so that the tensile direction was the rolling direction, and a tensile test was performed to determine the proportional limit of each steel sheet.
  • the proportional limit was obtained by performing a tensile test at a tensile speed of 1 mm / min using a tensile test piece in which a strain gauge having a length of 5 mm was attached to both sides of the parallel part.
  • the proportional limit is defined as a point at which the inclination starts to decrease as the stress increases due to the relationship between the inclination ( ⁇ / ⁇ ) of the stress-strain curve and the stress ( ⁇ ).
  • the obtained results are shown in FIG. 4 in relation to the proportional limit of the steel plate and the roll surface roughness Ra of the used roll.
  • roll surface roughness Ra was measured based on the prescription
  • FIG. 4 shows that the proportional limit of the steel sheet easily becomes 150 MPa or less when temper rolling is performed using a rolling roll having a roll surface roughness Ra of 2.0 ⁇ m or less.
  • the present invention has been completed based on such findings and further studies. That is, the gist of the present invention is as follows. (1) By mass%, C: 0.10% or less, Si: 0.05% or less, Mn: 0.1 to 1.0%, P: 0.05% or less, S: 0.02% or less, A composition comprising Al: 0.02 to 0.10%, N: less than 0.005%, the balance consisting of Fe and inevitable impurities, and a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 ⁇ m; A thin steel sheet obtained by subjecting a thin steel sheet having a surface roughness Ra to temper rolling using a rolling roll having a surface roughness Ra of 2.0 ⁇ m or less, and having a proportional limit of 150 MPa or less. Excellent cold rolled steel sheet.
  • the steel material is subjected to a hot-rolling step and a cold-rolling step in order to obtain a cold-rolled plate, and the cold-rolled plate is subjected to an annealing step to obtain a cold-rolled annealed plate.
  • the annealing step is performed on the cold-rolled sheet, annealing temperature: After heating for 30 s or more at a temperature in the range of 730 to 850 ° C., an annealing treatment is applied to cool to a temperature of 600 ° C.
  • a rolling roll having a surface roughness Ra of 2.0 ⁇ m or less is used, and the temper rolling elongation is d / 20 to d / 5 corresponding to the average crystal grain size d ( ⁇ m) of the cold-rolled annealed sheet.
  • % Cold rolled thin steel sheet excellent in shape freezing property characterized by being subjected to temper rolling to a range of% and producing a cold rolled thin steel sheet having a proportional limit of 150 MPa or less.
  • the cold-rolled sheet is annealed at a temperature in the range of 730 to 850 ° C. and 600 ° C. or less at an average cooling rate of 5 ° C./s or more.
  • the manufacturing method of the cold-rolled thin steel plate characterized by making it the annealing-hot-dip galvanization process process which cools to the temperature of this and performs hot-dip galvanization.
  • a cold-rolled thin steel sheet having a proportional limit of 150 MPa or less can be manufactured at low cost and stably, and the shape freezing property of the formed member can be remarkably improved, thereby producing a remarkable industrial effect.
  • C 0.10% or less
  • the content of C exceeding 0.10% makes ferrite grains finer, promotes the formation of cementite, makes it difficult to lower the proportional limit, increases hardenability, and lowers the temperature. Promotes the formation of the transformation phase, increases strength and decreases ductility. For this reason, C was limited to 0.10% or less. In addition, Preferably it is 0.05% or less. In the present invention, it is not necessary to limit the lower limit of the C content, but excessive reduction leads to an increase in production cost, so 0.0010% or more is preferable.
  • Si 0.05% or less
  • Si is an element that stabilizes ferrite, promotes the concentration of C in the ferrite, facilitates the formation of cementite, martensite, and the like, and contributes to the promotion of hardening. From the viewpoint of improving the property, it is preferable to reduce as much as possible. Moreover, Si forms Si oxide on the surface during annealing, and adversely affects surface properties, chemical conversion properties, plating properties, and the like. For these reasons, Si is limited to 0.05% or less. In addition, More preferably, it is 0.03% or less.
  • Mn 0.1 to 1.0%
  • Mn is an effective element that forms MnS and prevents hot cracking due to S, and is preferably contained according to the amount of S contained. In order to obtain such an effect, the content of 0.1% or more is required.
  • Mn is a solid solution that increases the strength of the steel and improves the hardenability and contributes to the refinement of crystal grains. A large amount of Mn causes the formation of low-temperature transformation phases such as martensite. It is difficult to promote or refine the ferrite grains to reduce the proportional limit, and to significantly reduce ductility and deteriorate workability. Such a tendency becomes prominent when the content exceeds 1.0%. For this reason, Mn was limited to the range of 0.1 to 1.0%. In applications where better workability is required, the content is desirably 0.5% or less.
  • P 0.05% or less
  • P is contained as an inevitable impurity in the steel, but has the effect of segregating at the grain boundaries and reducing the grain boundary strength. For this reason, although it is preferable to reduce as much as possible in this invention, 0.05% is accept
  • S 0.02% or less
  • S is an element that remarkably deteriorates the ductility of hot steel and induces hot cracking to significantly deteriorate the surface properties. Further, S forms coarse sulfides and lowers the ductility and toughness of steel. For this reason, it is preferable to reduce S as much as possible, but if it is up to about 0.02%, it is acceptable. Therefore, S is limited to 0.02% or less. In addition, Preferably it is 0.01% or less.
  • Al acts as a deoxidizer for steel, has the effect of improving the cleanliness of the steel, and has the effect of strongly fixing N and suppressing age hardening by N. In order to obtain such an effect, a content of 0.02% or more is required. On the other hand, inclusion exceeding 0.10% leads to deterioration of surface properties such as an increase in the amount of inclusions due to the formation of alumina. For this reason, Al was limited to the range of 0.02 to 0.10%. In addition, Preferably it is 0.05% or less.
  • N Less than 0.005% N is a solid solution that contributes to increasing the strength of the steel and has a tendency to increase the proportional limit. When it is contained in a large amount, it causes hot cracking of the slab, and the surface properties of the slab Although it is an element which has a tendency to deteriorate and it is desirable to reduce it as much as possible in the present invention, it is acceptable if it is less than 0.005%. For this reason, N was limited to less than 0.005%.
  • the above-mentioned components are basic components.
  • One or more selected from 0003 to 0.0030%, Cr: 0.1 to 1.0%, and Mo: 0.1 to 1.0% can be selected and contained.
  • Nb 0.010% or more
  • B 0.0003% or more
  • Cr 0.1% or more
  • Mo 0.1% or more
  • Ti 0.005 to 0.08%
  • Nb 0.010 to 0.030%
  • B 0.0003 to 0.0030%
  • Cr 0.1 to 1.%. It is preferable to limit to 0% and Mo: 0.1 to 1.0%, respectively.
  • the balance other than the components described above consists of Fe and inevitable impurities.
  • the thin steel sheet of the present invention has the above-described composition and further has a structure mainly composed of a ferrite phase having an average crystal grain size of 5 to 30 ⁇ m.
  • “mainly” refers to a case where the volume ratio with respect to the entire tissue is 95% or more, preferably 98% or more, more preferably 100%.
  • the second phase other than the main phase is cementite, pearlite, bainite, or the like.
  • the second phase has a volume ratio of 5% or less. When the amount of the second phase exceeds 5%, the steel plate becomes hard and formability (workability) decreases.
  • the average crystal grain size of the ferrite phase is less than 5 ⁇ m, the grain boundaries increase, so the strain during temper rolling is concentrated especially at the triple boundary of the grain boundaries, and the dislocations tend to become tandals. Tend to increase.
  • the average crystal grain size of the ferrite phase exceeds 30 ⁇ m and the crystal grains become coarse, unevenness called orange peel becomes prominent at the time of press molding, the surface property of the member is lowered, and the proportional limit is reduced. It becomes difficult to introduce necessary movable dislocations near the grain boundaries. For this reason, the average crystal grain size of the ferrite phase is limited to 5 to 30 ⁇ m.
  • the cold-rolled thin steel sheet of the present invention is a thin steel sheet obtained by subjecting a thin steel sheet having the above composition and the above structure to temper rolling using a rolling roll having a surface roughness Ra of 2.0 ⁇ m or less.
  • the surface roughness Ra of the rolling roll used for temper rolling is coarser than 2.0 ⁇ m, the strain introduced during temper rolling is concentrated on the surface layer of the steel sheet, and uniform strain can be introduced in the sheet thickness direction. In other words, the desired proportional limit cannot be reduced. For this reason, in this invention, it decided to perform the temper rolling which uses the rolling roll whose surface roughness Ra is 2.0 micrometers or less to the thin steel plate which has the above-mentioned composition and the above-mentioned structure.
  • a steel material is sequentially subjected to a hot rolling process, a cold rolling process, and an annealing process to obtain a cold rolled annealing sheet.
  • the steel material to be used is in mass%, C: 0.10% or less, Si: 0.05% or less, Mn: 0.1 to 1.0%, P: 0.0.
  • a steel material having a composition including more than seeds and the balance Fe and inevitable impurities is used.
  • the manufacturing method of the steel material is not particularly limited, but the molten steel having the above composition is melted by a conventional melting method such as a converter, and a steel material such as a slab by a conventional casting method such as a continuous casting method.
  • the steel material casting method is desirably an intermittent casting method in order to prevent macro segregation of components, but there is no problem with the ingot casting method or the thin slab casting method.
  • a hot rolling process and a cold rolling process are sequentially performed on the steel material having the above composition to obtain a cold rolled sheet.
  • the hot rolling process is not limited as long as the steel material is heated, subjected to hot rolling, and then subjected to a winding process to produce a hot-rolled sheet having a desired dimension and shape. Absent.
  • the obtained hot-rolled sheet is subjected to a cold-rolling step to obtain a cold-rolled sheet.
  • the hot rolled sheet is pickled and then cold rolled to obtain a cold rolled sheet.
  • any conventional pickling method can be applied.
  • the cold rolling should just be made into the cold-rolled board of a predetermined dimension shape, and all the normal cold rolling conditions can be applied.
  • the annealing process is a process in which the cold-rolled sheet is subjected to an annealing process of heating to a temperature of 600 ° C. or less at an average cooling rate of 5 ° C./s after heating the cold rolled sheet at a temperature in the range of 730 to 850 ° C. for 30 s or more.
  • a cold-rolled annealed plate having a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 ⁇ m is obtained.
  • the annealing temperature is less than 730 ° C., it is difficult to complete recrystallization of ferrite processed by cold rolling, and coarse ferrite grains having an average crystal grain size of 5 ⁇ m or more cannot be secured.
  • the annealing temperature is higher than 850 ° C., the transformation to austenite proceeds and transforms to fine ferrite during cooling, or transforms to a low temperature transformation phase, and the ferrite fraction decreases. Therefore, the annealing temperature is preferably limited to a temperature in the range of 730 to 850 ° C.
  • the holding (heating) time at the annealing temperature is preferably 30 s or more.
  • the upper limit of the heating time is not particularly limited, but is preferably about 200 s or less from the viewpoint of productivity.
  • the cooling after annealing in the annealing step is preferably performed from the annealing temperature to 600 ° C. or less at an average cooling rate of 5 ° C./s or more.
  • the cooling rate after annealing is less than 5 ° C./s on average, the growth of ferrite grains is promoted, and a ferrite structure having a desired grain size range cannot be obtained.
  • it is not necessary to limit the upper limit of the cold rolling rate after annealing but special cooling equipment is required for rapid cooling with rapid cooling exceeding 30 ° C./s, so cooling at 30 ° C./s or less. It is preferable to cool at a rate. If the cooling stop temperature exceeds 600 ° C.
  • a low temperature transformation phase may be formed by subsequent cooling. For this reason, cooling after annealing was decided to cool to 600 ° C. or lower at an average cooling rate of 5 ° C./s or higher. In addition, it is not necessary to prescribe
  • the cold-rolled sheet is annealed at a temperature in the range of 730 to 850 ° C., and the average cooling rate of 5 ° C./s or more is 600 ° C. or less. It is good also as an annealing-hot galvanization process process which cools to temperature and performs hot dip galvanization.
  • a hot dip galvanizing treatment may be performed by continuously dipping in a normal hot dip galvanizing bath near 480 ° C. using a continuous hot dip galvanizing line.
  • a plating layer alloying treatment step may be performed in which the hot dip galvanized layer is an alloyed hot dip galvanized layer.
  • the alloying treatment may be a reheating treatment in a temperature range of 500 ° C. or higher and lower than 600 ° C. according to a conventional method.
  • a cold-rolled annealed plate (plated plate) that has undergone such a hot-rolling step, a cold-rolling step, an annealing step, or an annealing-hot-dip galvanizing treatment step is mainly composed of a ferrite phase having an average crystal grain size of 5 ⁇ m to 30 ⁇ m. It becomes a cold-rolled annealed plate (plated plate) having a texture to be formed. In addition, you may form a chemical conversion treatment film in the obtained cold-rolled annealing board (plating board) further.
  • the cold-rolled annealed plate (plated plate) is then subjected to temper rolling using a rolling roll having a surface roughness Ra of 2.0 ⁇ m or less.
  • the surface roughness Ra of the rolling roll to be used exceeds 2.0 ⁇ m, the proportional limit of 150 MPa or less cannot be stably secured as shown in FIG.
  • the lower limit of the surface roughness Ra of the rolling roll to be used is not particularly limited. However, when the surface roughness Ra of the rolling roll to be used is reduced, the surface roughness of the obtained steel sheet is also reduced, and the frictional resistance of the steel sheet is reduced. Thus, when the coil is wound up, the coil is easily wound and crushed easily. For this reason, it is preferable that surface roughness Ra of the rolling roll to be used shall be 0.2 micrometer or more. In addition, the surface roughness Ra shall use the value measured based on prescription
  • the elongation ratio (temper rolling elongation ratio) R (%) in temper rolling is (0.05 to 0. 0), where d ( ⁇ m) is the average crystal grain size of the cold-rolled annealed sheet as the material to be rolled. 20) It is good to set it as d.
  • the reason is as follows. By applying temper rolling, movable dislocations are introduced and the proportional limit is reduced. However, movable dislocations introduced by temper rolling are likely to be introduced in the vicinity of grain boundaries. Therefore, in order to effectively introduce movable dislocations necessary for reducing the desired proportional limit to the vicinity of grain boundaries, the larger the ferrite grain size, It is necessary to increase the temper rolling elongation.
  • FIG. 5 shows the relationship between the proportional limit (MPa) of the temper-rolled steel sheet and R / d.
  • FIG. 5 shows the result of temper rolling using a steel sheet having an average ferrite grain size d of 5 to 20 ⁇ m and a rolling roll having a surface roughness Ra of 0.2 to 1.8 ⁇ m.
  • FIG. 5 shows that the proportional limit of the steel sheet is 150 MPa or less when R / d is between 0.05 and 0.20.
  • the temper rolling elongation rate R (%) is less than 0.05 d, the rolling amount of the temper rolling is insufficient, the desired movable dislocation cannot be introduced, and the desired low proportional limit cannot be ensured.
  • the amount of reduction exceeds 0.20d, the introduced dislocations are tangled, and the movable dislocation that effectively contributes to the reduction of the proportional limit is insufficient, and a desired low proportional limit cannot be secured.
  • the temper rolling elongation rate R (%) was limited to the range of (0.05-0.20) d corresponding to the ferrite average crystal grain size d.
  • a steel material having the composition shown in Table 1 is heated to 1200 ° C., subjected to hot rolling at a final pass exit temperature of 900 ° C., wound at 550 ° C., and a sheet thickness of 2.6 mm.
  • a hot rolling process was applied.
  • the obtained thin hot-rolled sheet was pickled and then cold-rolled to give a cold-rolled step of forming a cold-rolled sheet having a thickness of 0.8 mm.
  • the obtained cold-rolled sheet was subjected to an annealing process in which annealing treatment was performed under the conditions of annealing temperature, holding time, and cooling rate shown in Table 2 to obtain a thin cold-rolled annealed sheet.
  • the cooling rate was an average from the annealing temperature to 600 ° C.
  • Some steel sheets were subjected to an annealing-hot dip galvanizing process under the conditions shown in Table 2 instead of the annealing process.
  • a hot dip galvanizing treatment in which the plating bath was continuously immersed in a hot dip galvanizing bath at a temperature of 480 ° C. was performed following the annealing treatment.
  • Some steel sheets were subjected to alloying treatment at the temperatures shown in Table 2 after the hot dip galvanizing treatment.
  • the particle size and the texture fraction were determined.
  • the average crystal grain size of the ferrite phase was determined by a cutting method for an area of 200 ⁇ 200 ⁇ m using an optical microscope (magnification: 100 times).
  • the structure fraction of the ferrite phase was calculated using an image analysis apparatus by capturing two images of a 200 ⁇ 200 ⁇ m region using an optical microscope (magnification: 100 times). The second phase other than ferrite was also observed.
  • Table 2 The structure observation results are also shown in Table 2.
  • the obtained cold-rolled annealed plate (plated plate) was tempered with a temper rolling elongation R (%) shown in Table 2 using a rolling roll having a surface roughness Ra ( ⁇ m) shown in Table 2.
  • the surface roughness Ra of the rolling roll was measured in accordance with the provisions of JIS B 0601-2001.
  • electrogalvanizing treatment was performed after temper rolling.
  • a JIS No. 5 test piece (GL: 50 mm) is sampled from a temper-rolled thin steel sheet (thin-plated steel sheet) so that the test direction is the rolling direction, and a tensile test is performed in accordance with the provisions of JIS Z 2241.
  • Tensile properties (yield strength YS, tensile strength TS, elongation El) were determined. Further, from the obtained thin steel sheet, a JIS No. 5 test piece was sampled so that the test direction was the rolling direction, and a tensile test was performed to obtain a proportional limit. The proportional limit is determined by performing a tensile test at a tensile speed of 1 mm / min using a tensile test piece affixed to strain gauges (gauge length: 5 mm) on both sides of the parallel portion, and the slope of the stress-strain curve ( ⁇ / ⁇ ). It calculated
  • All of the examples of the present invention are thin steel sheets having a structure mainly composed of a ferrite phase having an average crystal grain size of 5 to 30 ⁇ m and a low proportional limit of 150 MPa or less.
  • the proportional limit exceeds 150 MPa.

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Abstract

Disclosed are: a thin steel sheet having a low proportional limit; and a process for producing the thin steel sheet. A cold-rolled steel sheet, which has a chemical composition comprising, in mass%, 0.10% or less of C, 0.05% or less of Si, 0.1-1.0% of Mn, 0.05% or less of P, 0.02% or less of S, 0.02-0.10% of Al, less than 0.005% of N and a remainder made up by Fe and unavoidable impurities, is subjected to an annealing treatment which comprises heating at an annealing temperature of 730-850˚C for 30 s or longer and cooling to a temperature equal to or lower than 600˚C at a cooling rate of 5˚C/s or more, thereby producing a cold-rolled annealed sheet having a structure mainly composed of a ferrite phase having an average crystal grain diameter (d) of 5-30 μm. The cold-rolled annealed sheet is subjected to a temper rolling treatment using a roll having a surface roughness (Ra) of 2.0 μm or less and at a temper rolling stretch ratio (R) (%) of (0.05-0.20)d (wherein d (μm) represents the average crystal grain diameter of the thin cold-rolled annealed sheet). In this manner, a cold-rolled thin steel sheet having a proportional limit of 150 MPa or less can be produced. The cold-rolled thin steel sheet may have, formed on the surface thereof, a molten zinc plated layer, an alloyed molten zinc plated layer or an electrolytic zinc plated layer.

Description

形状凍結性に優れた冷延薄鋼板およびその製造方法Cold-rolled thin steel sheet having excellent shape freezing property and manufacturing method thereof
　本発明は、電化製品、事務用機器、自動車用部材等の構造部材用として好適な、冷延薄鋼板に係り、とくに、プレス成形後の高寸法精度が要求される部材用として好適な、形状凍結性に優れた冷延薄鋼板に関する。なお、ここでいう「薄鋼板」は、板厚：０．２~２．０ｍｍの鋼板で、鋼板および鋼帯を含むものとする。 The present invention relates to a cold-rolled thin steel sheet suitable for structural members such as electrical appliances, office equipment, and automobile members, and particularly suitable for members requiring high dimensional accuracy after press forming. The present invention relates to a cold-rolled thin steel sheet having excellent freezing properties. Here, the “thin steel plate” is a steel plate having a thickness of 0.2 to 2.0 mm, and includes a steel plate and a steel strip.
　近年、電機分野等の分野では、原料価格の高騰に伴い、コスト低減のために、安価な素材が強く要求され、素材として使用する鋼板の薄肉化が加速している。また、自動車分野では、コスト低減に加えて、地球環境の保全という観点から、自動車の燃費向上が強く要求され、自動車車体の軽量化のために、素材である鋼板の薄肉化が進められている。
　しかし、素材の薄肉化により素材板厚を減少すると、製品（部材）の剛性が低下するという問題がある。このような問題に対し、部材にビードを付与したり、部材形状を見直したりして、断面二次モーメントが大きくなるように工夫し、所望の剛性を確保する場合が多くなっている。その結果、部材形状が複雑となり、プレス成形時に成形される部位が増加し、製品（部材）形状にゆがみが生じやすくなるという問題がある。製品（部品）形状にゆがみが生じた場合には、形状を矯正するため再プレス成形する必要がある。しかし、再プレス成形を行うことは、製造コストの増加を招くため、プレス成形後の形状凍結性に優れた鋼板が強く要望されるようになっている。 In recent years, in the field of electrical machinery and the like, with the soaring raw material price, an inexpensive material is strongly demanded for cost reduction, and the thinning of the steel plate used as the material is accelerating. In the automotive field, in addition to cost reduction, from the viewpoint of global environmental conservation, there is a strong demand for improved fuel economy of automobiles, and steel sheets, which are raw materials, are being made thinner to reduce the weight of automobile bodies. .
However, when the thickness of the material is reduced by reducing the thickness of the material, there is a problem that the rigidity of the product (member) is lowered. In response to such problems, there are many cases where a desired rigidity is secured by giving a bead to the member or revising the member shape so as to increase the second moment of section. As a result, there is a problem that the member shape becomes complicated, the number of parts formed during press molding increases, and the product (member) shape tends to be distorted. If the product (part) shape is distorted, it must be re-pressed to correct the shape. However, since re-press forming causes an increase in manufacturing cost, a steel sheet excellent in shape freezing property after press forming has been strongly demanded.
　このような要望に対し、例えば、特許文献１には、｛１００｝＜０１１＞~｛２２３｝＜１１０＞方位群のＸ線ランダム強度比の平均値が３．０以上で、かつ｛５５４｝＜２２５＞、｛１１１｝＜１１２＞、｛１１１｝＜１１０＞の３つの結晶方位のＸ線ランダム強度比の平均値が３．５以下である特定方位の集合組織を発達させ、さらに圧延方向のｒ値および圧延方向と直角方向のｒ値のうち少なくとも一つが０．７以下である、曲げ加工を主とする、形状凍結性に優れたフェライト系薄鋼板が記載されている。特許文献１に記載された鋼板は、曲げ成形性が著しく向上し、スプリングバック量が少なく、曲げ加工を主とする、形状凍結性に優れるとしている。 In response to such a request, for example, Patent Document 1 discloses that the average value of the X-ray random intensity ratio of {100} <011> to {223} <110> orientation group is 3.0 or more and {554} <225>, {111} <112>, {111} <110> Three crystal orientations of X-ray random intensity ratio of the average value of 3.5 or less to develop a texture with a specific orientation, further rolling direction A ferritic thin steel sheet having excellent shape freezing properties, mainly bending, in which at least one of the r value and the r value perpendicular to the rolling direction is 0.7 or less is described. The steel sheet described in Patent Document 1 is markedly improved in bend formability, has a small amount of springback, and is excellent in shape freezing, mainly bending.
　また、特許文献２には、フェライト基地中にマルテンサイトを含む島状組織が分散した組織を有し、表面平均あらさＨａ０．４~１．８μｍで、ＰＰＩ値が０．５μｍカウントレベルで８０以上の表面粗度を有し、かつ比例限界応力が２０ｋｇ／ｍｍ２以下、即ち２００ＭＰａ以下である、形状凍結性に優れた高張力鋼板が記載されている。これにより、プレス成形時のポンチ面と鋼板とのなじみ性が向上し、プレス成形後の形状凍結性に優れた部材（製品）が得られるとしている。 Further, Patent Document 2 has a structure in which an island-like structure including martensite is dispersed in a ferrite matrix, the surface average roughness Ha is 0.4 to 1.8 μm, and the PPI value is 80 or more at a 0.5 μm count level. A high-tensile steel sheet having excellent surface freezing property and having a surface roughness of 20 kg / mm 2 or less, that is, 200 MPa or less, is described. Thereby, the conformability between the punch surface and the steel sheet during press forming is improved, and a member (product) having excellent shape freezing property after press forming is obtained.
特開２００１−３０３１７５公報JP 2001-303175 A 特開昭５８−２５４５６号公報JP 58-25456 A
　しかし、特許文献１に記載された技術により製造された鋼板では、主として曲げ加工を受ける製品（部材）においては、所望の形状凍結性を確保できるが、例えば張出し加工のような、曲げ加工以外の加工を受ける製品（部材）においては、必ずしも満足できる形状凍結性を確保できていないという問題があった。また、特許文献２に記載された技術により製造された鋼板では、フェライト基地中にマルテンサイトを含む島状組織を分散させた組織とするため、硬質化した鋼板となりやすく、張出し高さの高い成形の場合には、割れが発生する場合が多いという問題があった。 However, in a steel sheet manufactured by the technique described in Patent Document 1, a desired shape freezing property can be secured in a product (member) that is mainly subjected to bending, but other than bending, such as overhanging, for example. In products (members) subjected to processing, there has been a problem that satisfactory shape freezing properties cannot always be secured. Moreover, in the steel plate manufactured by the technique described in Patent Document 2, since the island-like structure containing martensite is dispersed in the ferrite matrix, the steel plate tends to be hardened and formed with a high overhang height. In this case, there is a problem that cracks often occur.
　本発明は、かかる従来技術の問題を解決し、形状凍結性に優れた冷延薄鋼板およびその製造方法を提案することを目的とする。 The object of the present invention is to solve the problems of the prior art and propose a cold-rolled thin steel sheet having excellent shape freezing property and a method for producing the same.
　上記した目的を達成するために、本発明者らは、形状凍結性に及ぼす各種要因について、鋭意研究した。本発明者らは、プレス成形時の製品（部材）の形状不良は、プレス成形時に導入された弾性歪が、プレス金型から製品（部材）を取り出すときに開放されることにより生じると考え、鋼板の比例限度に着目した。 In order to achieve the above-described object, the present inventors have intensively studied various factors affecting the shape freezing property. The present inventors consider that the defective shape of the product (member) at the time of press molding is caused by the elastic strain introduced at the time of press molding being released when the product (member) is taken out from the press mold, We focused on the proportional limit of the steel sheet.
　比例限度とは、弾性体に外力を加えたときに、ひずみと比例関係を保つことができる応力の限度をいう。応力が小さい間は、フックの法則が成り立つので、比例関係がみられる。各種比例限度を有する鋼板を用意し、プレス成形により所定形状の部品を成形し、成形後の形状凍結性について調査した。その結果、所望の優れた形状凍結性を確保するためには、鋼板の比例限度を１５０ＭＰａ以下に低減する必要のあることを知見した。 The proportional limit is the limit of stress that can maintain a proportional relationship with strain when an external force is applied to the elastic body. While the stress is small, Hooke's law holds, so a proportional relationship is seen. Steel plates having various proportional limits were prepared, parts of a predetermined shape were formed by press forming, and the shape freezing property after forming was investigated. As a result, it was found that the proportional limit of the steel plate needs to be reduced to 150 MPa or less in order to ensure the desired excellent shape freezing property.
　本発明の基礎となった実験結果について説明する。
　各種比例限度を有する板厚：０．８ｍｍの薄鋼板（試験材）をプレス成形し、図１に示す寸法のハット形状の部品とした。なお、しわ押さえ圧は２０ｔｏｎとした。成形後、金型から部品を取り出し、ハット形状の開き量Ｘを測定した。図２に、鋼板の比例限度と開き量Ｘとの関係を示す。図２から、鋼板の比例限度が１５０ＭＰａ以下であれば、開き量Ｘの増加は少なく、優れた形状凍結性を保持できているが、鋼板の比例限度が１５０ＭＰａを上回り、大きくなると、開き量Ｘは急激に増大し、形状凍結性が著しく低下することがわかる。 The experimental results on which the present invention is based will be described.
A thin steel plate (test material) having a thickness of 0.8 mm having various proportional limits was press-molded to obtain a hat-shaped part having the dimensions shown in FIG. The wrinkle pressing pressure was 20 tons. After molding, the part was taken out from the mold, and the opening X of the hat shape was measured. In FIG. 2, the relationship between the proportional limit of a steel plate and the opening amount X is shown. From FIG. 2, if the proportional limit of the steel plate is 150 MPa or less, the increase in the opening amount X is small and excellent shape freezing property can be maintained, but if the proportional limit of the steel plate exceeds 150 MPa and becomes large, the opening amount X Increases rapidly and the shape freezing property is remarkably lowered.
　つぎに、本発明者らは、上記した比例限度を有する鋼板を安定して製造するために、鋼板の比例限度に及ぼす各種要因について鋭意研究した。その結果、比較的大きな結晶粒径を有するフェライト相を主体とする鋼板に、表面粗さの小さいロールを用いた調質圧延を施すことにより、容易に比例限度を低減できることを見出した。
　つぎに、上記した知見の基礎となった実験結果について説明する。 Next, the present inventors diligently studied various factors affecting the proportional limit of the steel sheet in order to stably manufacture the steel sheet having the proportional limit described above. As a result, it was found that the proportional limit can be easily reduced by subjecting a steel sheet mainly composed of a ferrite phase having a relatively large crystal grain size to temper rolling using a roll having a small surface roughness.
Next, experimental results that serve as a basis for the above-described knowledge will be described.
　質量％で、０．０４０％Ｃ−０．０１％Ｓｉ−０．２０％Ｍｎ−０．０１％Ｐ−０．０１％Ｓ−０．０４％Ａｌ‐０．００３％Ｎ‐残部Ｆｅの組成を有し、平均結晶粒径：１０μｍのフェライト単相からなる組織を有する冷延焼鈍板（板厚：０．８ｍｍ）に、圧延伸び率１％の調質圧延を施した。調質圧延に際しては、表面粗さＲａを０．２~２．５μｍに調整した各種圧延ロールを使用した。調質圧延済み各鋼板からそれぞれ、引張方向が圧延方向となるようにＪＩＳ　５号試験片を採取し、引張試験を実施し、各鋼板の比例限度を求めた。 Composition of 0.040% C-0.01% Si-0. 20% Mn-0.01% P-0.01% S-0.04% Al-0.003% N-balance Fe in mass% A cold-rolled annealed plate (thickness: 0.8 mm) having a structure composed of a ferrite single phase with an average crystal grain size of 10 μm was subjected to temper rolling with a rolling elongation of 1%. In temper rolling, various rolling rolls having a surface roughness Ra adjusted to 0.2 to 2.5 μm were used. A JIS No. 5 test piece was taken from each temper-rolled steel sheet so that the tensile direction was the rolling direction, and a tensile test was performed to determine the proportional limit of each steel sheet.
　比例限度は、平行部両面に長さ５ｍｍの歪ゲージを貼付した引張試験片を用いて、引張速度：１ｍｍ／ｍｉｎで引張試験を行って求めた。比例限度は、図３に示すように、応力−歪曲線の傾き（Δσ／Δε）と応力（σ）との関係から、応力増加により傾きが小さくなり始める点とした。
　得られた結果を、鋼板の比例限度と使用した圧延ロールのロール表面粗さＲａとの関係で、図４に示す。なお、ロール表面粗さＲａは、ＪＩＳ　Ｂ　０６０１−２００１の規定に準拠して測定した。図４から、ロール表面粗さＲａが２．０μｍ以下の圧延ロールを使用して調質圧延を施せば、容易に鋼板の比例限度が１５０ＭＰａ以下となることがわかる。 The proportional limit was obtained by performing a tensile test at a tensile speed of 1 mm / min using a tensile test piece in which a strain gauge having a length of 5 mm was attached to both sides of the parallel part. As shown in FIG. 3, the proportional limit is defined as a point at which the inclination starts to decrease as the stress increases due to the relationship between the inclination (Δσ / Δε) of the stress-strain curve and the stress (σ).
The obtained results are shown in FIG. 4 in relation to the proportional limit of the steel plate and the roll surface roughness Ra of the used roll. In addition, roll surface roughness Ra was measured based on the prescription | regulation of JISB0601-2001. FIG. 4 shows that the proportional limit of the steel sheet easily becomes 150 MPa or less when temper rolling is performed using a rolling roll having a roll surface roughness Ra of 2.0 μm or less.
　上記した表面粗さの小さいロールを使用した調質圧延による比例限度減少の機構については、現在までに十分にその詳細を解明できていないが、本発明者らはつぎのように推定している。
　結晶粒径５~３０μｍの粗大なフェライトを主体とする鋼板に、Ｒａが２．０μｍ以下の小さな表面粗さの圧延ロールを用いて調質圧延を施せば、板厚方向に均一な歪を導入することができ、さらにフェライト結晶粒内への可動転位の導入が促進でき、比例限度を顕著に低減できるものと考えている。一方、表面粗さＲａが２．０μｍを超えて大きな表面粗さの圧延ロールを用いて調質圧延を行った場合には、導入される歪が鋼板表層に集中するため、転位がタングル化して可動転位が減少し、比例限度の低減が得られなくなったものと考えられる。 About the mechanism of the proportional limit reduction by the temper rolling using the roll with the small surface roughness described above, the details have not been clarified until now, but the present inventors presume as follows.
If a steel sheet mainly composed of coarse ferrite with a crystal grain size of 5 to 30μm is temper-rolled using a roll having a small surface roughness with a Ra of 2.0μm or less, uniform strain is introduced in the thickness direction. Further, it is considered that the introduction of movable dislocations into ferrite crystal grains can be promoted, and the proportional limit can be significantly reduced. On the other hand, when temper rolling is performed using a rolling roll having a surface roughness Ra exceeding 2.0 μm and a large surface roughness, the introduced strain concentrates on the surface layer of the steel sheet, so that the dislocations are tangled. It is considered that the movable dislocation decreased and the proportional limit could not be reduced.
　本発明は、かかる知見に基づき、さらに検討を加えて完成されたものである。すなわち、本発明の要旨は次のとおりである。
　（１）質量％で、Ｃ：０．１０％以下、Ｓｉ：０．０５％以下、Ｍｎ：０．１~１．０％、Ｐ：０．０５％以下、Ｓ：０．０２％以下、Ａｌ：０．０２~０．１０％、Ｎ：０．００５％未満を含み、残部Ｆｅおよび不可避的不純物からなる組成と、平均結晶粒径ｄ：５~３０μｍのフェライト相を主体とする組織とを有する薄鋼板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用した調質圧延を施してなる薄鋼板であって、１５０ＭＰａ以下の比例限度を有することを特徴とする形状凍結性に優れた冷延薄鋼板。 The present invention has been completed based on such findings and further studies. That is, the gist of the present invention is as follows.
(1) By mass%, C: 0.10% or less, Si: 0.05% or less, Mn: 0.1 to 1.0%, P: 0.05% or less, S: 0.02% or less, A composition comprising Al: 0.02 to 0.10%, N: less than 0.005%, the balance consisting of Fe and inevitable impurities, and a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 μm; A thin steel sheet obtained by subjecting a thin steel sheet having a surface roughness Ra to temper rolling using a rolling roll having a surface roughness Ra of 2.0 μm or less, and having a proportional limit of 150 MPa or less. Excellent cold rolled steel sheet.
　（２）（１）において、前記組成に加えてさらに、質量％で、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を含有する組成とすることを特徴とする冷延薄鋼板。
　（３）（１）または（２）に記載の冷延薄鋼板の少なくとも一方の表面に、溶融亜鉛めっき層、合金化溶融亜鉛めっき層、または電気亜鉛めっき層を形成してなることを特徴とする形状凍結性に優れた冷延薄鋼板。 (2) In (1), in addition to the above composition, in terms of mass%, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0003 to 0.0030 %, Cr: 0.1 to 1.0%, Mo: 0.1 to 1.0%, or a composition containing one or more selected from the group consisting of 0.1 to 1.0% .
(3) A hot-dip galvanized layer, an alloyed hot-dip galvanized layer, or an electrogalvanized layer is formed on at least one surface of the cold-rolled thin steel sheet according to (1) or (2). Cold rolled thin steel sheet with excellent shape freezing properties.
　（４）鋼素材に熱延工程と、冷延工程とを順次施し冷延板とし、該冷延板に焼鈍工程を施し冷延焼鈍板とする冷延薄鋼板の製造方法において、前記鋼素材が、質量％で、Ｃ：０．１０％以下、Ｓｉ：０．０５％以下、Ｍｎ：０．１~１．０％、Ｐ：０．０５％以下、Ｓ：０．０２％以下、Ａｌ：０．０２~０．１０％、Ｎ：０．００５％未満を含み、残部Ｆｅおよび不可避的不純物からなる組成を有する鋼素材であり、前記焼鈍工程が、前記冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で３０ｓ以上加熱したのち、５℃／ｓ以上の平均冷却速度で６００℃以下の温度まで冷却する焼鈍処理を施し、平均結晶粒径ｄ：５~３０μｍのフェライト相を主体とする組織を有する冷延焼鈍板とする工程であり、前記焼鈍工程後に、前記冷延焼鈍板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用し、調質圧延伸び率を、該冷延焼鈍板の平均結晶粒径ｄ（μｍ）に対応して、ｄ／２０~ｄ／５％の範囲とする調質圧延を施し、比例限度が１５０ＭＰａ以下である冷延薄鋼板とすることを特徴とする、形状凍結性に優れた冷延薄鋼板の製造方法。 (4) In the method of manufacturing a cold-rolled thin steel sheet, the steel material is subjected to a hot-rolling step and a cold-rolling step in order to obtain a cold-rolled plate, and the cold-rolled plate is subjected to an annealing step to obtain a cold-rolled annealed plate. Is, by mass%, C: 0.10% or less, Si: 0.05% or less, Mn: 0.1 to 1.0%, P: 0.05% or less, S: 0.02% or less, Al : 0.02 to 0.10%, N: less than 0.005%, a steel material having a composition consisting of the balance Fe and inevitable impurities, the annealing step is performed on the cold-rolled sheet, annealing temperature: After heating for 30 s or more at a temperature in the range of 730 to 850 ° C., an annealing treatment is applied to cool to a temperature of 600 ° C. or less at an average cooling rate of 5 ° C./s or more, and a ferrite phase having an average crystal grain size d: 5 to 30 μm A cold-rolled annealed plate having a structure mainly composed of In addition, a rolling roll having a surface roughness Ra of 2.0 μm or less is used, and the temper rolling elongation is d / 20 to d / 5 corresponding to the average crystal grain size d (μm) of the cold-rolled annealed sheet. % Cold rolled thin steel sheet excellent in shape freezing property, characterized by being subjected to temper rolling to a range of% and producing a cold rolled thin steel sheet having a proportional limit of 150 MPa or less.
　（５）（４）において、前記焼鈍工程に代えて、前記冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で焼鈍して、５℃／ｓ以上の平均冷却速度で６００℃以下の温度まで冷却し、溶融亜鉛めっきを施す焼鈍−溶融亜鉛めっき処理工程とすることを特徴とする冷延薄鋼板の製造方法。
　（６）（５）において前記焼鈍−溶融亜鉛めっき処理工程を経たのち、さらに溶融亜鉛めっきを合金化処理する合金化処理工程を施すことを特徴とする冷延薄鋼板の製造方法。 (5) In (4), in place of the annealing step, the cold-rolled sheet is annealed at a temperature in the range of 730 to 850 ° C. and 600 ° C. or less at an average cooling rate of 5 ° C./s or more. The manufacturing method of the cold-rolled thin steel plate characterized by making it the annealing-hot-dip galvanization process process which cools to the temperature of this and performs hot-dip galvanization.
(6) A method for producing a cold-rolled thin steel sheet, wherein after the annealing-hot dip galvanizing treatment step in (5), an alloying treatment step of alloying the hot dip galvanizing is performed.
　（７）（４）ないし（６）のいずれかにおいて、前記鋼素材の組成に加えてさらに、質量％で、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を含有する組成とすることを特徴とする冷延薄鋼板の製造方法。 (7) In any one of (4) to (6), in addition to the composition of the steel material, in addition to mass, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030% B: 0.0003 to 0.0030%, Cr: 0.1 to 1.0%, Mo: a composition containing one or more selected from 0.1 to 1.0%; A method for producing a cold-rolled thin steel sheet.
　本発明によれば、比例限度が１５０ＭＰａ以下の冷延薄鋼板を安価にしかも安定して製造でき、成形後の部材の形状凍結性が格段に向上し、産業上格段の効果を奏する。 According to the present invention, a cold-rolled thin steel sheet having a proportional limit of 150 MPa or less can be manufactured at low cost and stably, and the shape freezing property of the formed member can be remarkably improved, thereby producing a remarkable industrial effect.
ハット状部品の形状寸法を模式的に示す説明図である。It is explanatory drawing which shows typically the shape dimension of hat-shaped components. ハット状部品の開き量Ｘに及ぼす鋼板の比例限度の影響を示すグラフである。It is a graph which shows the influence of the proportional limit of the steel plate on the opening amount X of a hat-shaped part. 応力−歪曲線の傾き（Δσ／Δε）と応力（σ）との関係から、比例限度の決定の一例を示すグラフである。It is a graph which shows an example of the determination of a proportional limit from the relationship between the inclination (Δσ / Δε) of a stress-strain curve and the stress (σ). 比例限度に及ぼすロール表面粗さＲａの影響を示すグラフである。It is a graph which shows the influence of roll surface roughness Ra which has on a proportional limit. 調質圧延済み鋼板の比例限度（ＭＰａ）とＲ／ｄとの関係を示す。The relationship between the proportional limit (MPa) of a temper-rolled steel plate and R / d is shown.
　まず、本発明薄鋼板の組成限定理由について説明する。以下、とくに断わらないかぎり質量％は、単に％で記す。
　Ｃ：０．１０％以下
　０．１０％を超えるＣの含有は、フェライト粒を微細化し、セメンタイトの形成を促進して、比例限度を低下させることを困難にするとともに、焼入れ性を高め、低温変態相の生成を促進して、強度を増加させ延性を低下させる。このため、Ｃは０．１０％以下に限定した。なお、好ましくは０．０５％以下である。本発明ではＣ含有量の下限を限定する必要はないが、過剰な低減は製造コストの高騰を招くため、０．００１０％以上とすることが好ましい。 First, the reason for limiting the composition of the thin steel sheet of the present invention will be described. Hereinafter, unless otherwise specified, mass% is simply expressed as%.
C: 0.10% or less The content of C exceeding 0.10% makes ferrite grains finer, promotes the formation of cementite, makes it difficult to lower the proportional limit, increases hardenability, and lowers the temperature. Promotes the formation of the transformation phase, increases strength and decreases ductility. For this reason, C was limited to 0.10% or less. In addition, Preferably it is 0.05% or less. In the present invention, it is not necessary to limit the lower limit of the C content, but excessive reduction leads to an increase in production cost, so 0.0010% or more is preferable.
　Ｓｉ：０．０５％以下
　Ｓｉは、フェライト安定化元素であり、フェライト中のＣの濃化を促進し、セメンタイト、マルテンサイト等を生成しやすくして硬質化促進に寄与する元素であり、加工性の向上の観点からはできるだけ低減することが好ましい。また、Ｓｉは、焼鈍時に表面にＳｉ酸化物を形成し、表面性状、化成処理性、めっき性等に悪影響を与える。このようなことから、Ｓｉは０．０５％以下に限定した。なお、より好ましくは０．０３％以下である。 Si: 0.05% or less Si is an element that stabilizes ferrite, promotes the concentration of C in the ferrite, facilitates the formation of cementite, martensite, and the like, and contributes to the promotion of hardening. From the viewpoint of improving the property, it is preferable to reduce as much as possible. Moreover, Si forms Si oxide on the surface during annealing, and adversely affects surface properties, chemical conversion properties, plating properties, and the like. For these reasons, Si is limited to 0.05% or less. In addition, More preferably, it is 0.03% or less.
　Ｍｎ：０．１~１．０％
　Ｍｎは、ＭｎＳを形成し、Ｓによる熱間割れを防止する有効な元素であり、含有するＳ量に応じて含有させることが好ましい。このような効果を得るためには、０．１％以上の含有を必要とする。また、Ｍｎは、固溶して鋼の強度を増加させるとともに、焼入れ性を向上させ、結晶粒の微細化に寄与する元素であり、多量の含有は、マルテンサイト等の低温変態相の生成を促進させたり、フェライト粒を微細化し、比例限度を低下させることを困難とするとともに、著しく延性を低下させて加工性を劣化させる。このような傾向は、１．０％を超えて含有する場合に顕著になる。このため、Ｍｎは０．１~１．０％の範囲に限定した。なお、より良好な加工性が要求される用途では、０．５％以下とすることが望ましい。 Mn: 0.1 to 1.0%
Mn is an effective element that forms MnS and prevents hot cracking due to S, and is preferably contained according to the amount of S contained. In order to obtain such an effect, the content of 0.1% or more is required. Mn is a solid solution that increases the strength of the steel and improves the hardenability and contributes to the refinement of crystal grains. A large amount of Mn causes the formation of low-temperature transformation phases such as martensite. It is difficult to promote or refine the ferrite grains to reduce the proportional limit, and to significantly reduce ductility and deteriorate workability. Such a tendency becomes prominent when the content exceeds 1.0%. For this reason, Mn was limited to the range of 0.1 to 1.0%. In applications where better workability is required, the content is desirably 0.5% or less.
　Ｐ：０．０５％以下
　Ｐは、鋼中に不可避的不純物として含有されるが、粒界に偏析して粒界強度を低下させる作用を有する。このため、本発明ではできるだけ低減することが好ましいが、０．０５％までは許容できる。このため、Ｐは０．０５％以下に限定した。なお、好ましくは０．０３％以下である。 P: 0.05% or less P is contained as an inevitable impurity in the steel, but has the effect of segregating at the grain boundaries and reducing the grain boundary strength. For this reason, although it is preferable to reduce as much as possible in this invention, 0.05% is accept | permitted. For this reason, P was limited to 0.05% or less. In addition, Preferably it is 0.03% or less.
　Ｓ：０．０２％以下
　Ｓは、熱間での鋼の延性を著しく低下させ、熱間割れを誘発して表面性状を著しく劣化させる元素である。また、Ｓは粗大な硫化物を形成し、鋼の延性、靭性を低下させる。このため、Ｓはできるだけ低減することが好ましいが、０．０２％程度までであれば、許容できる。このようなことから、Ｓは０．０２％以下に限定した。なお、好ましくは０．０１％以下である。 S: 0.02% or less S is an element that remarkably deteriorates the ductility of hot steel and induces hot cracking to significantly deteriorate the surface properties. Further, S forms coarse sulfides and lowers the ductility and toughness of steel. For this reason, it is preferable to reduce S as much as possible, but if it is up to about 0.02%, it is acceptable. Therefore, S is limited to 0.02% or less. In addition, Preferably it is 0.01% or less.
　Ａｌ：０．０２~０．１０％
　Ａｌは、鋼の脱酸剤として作用し、鋼の清浄度を向上させる作用を有するとともに、強力にＮを固定し、Ｎによる時効硬化を抑制する作用を有する。このような効果を得るためには０．０２％以上の含有を必要とする。一方、０．１０％を超える含有は、アルミナの生成による介在物量の増加など、表面性状の悪化に繋がる。このため、Ａｌは０．０２~０．１０％の範囲に限定した。なお、好ましくは０．０５％以下である。 Al: 0.02 to 0.10%
Al acts as a deoxidizer for steel, has the effect of improving the cleanliness of the steel, and has the effect of strongly fixing N and suppressing age hardening by N. In order to obtain such an effect, a content of 0.02% or more is required. On the other hand, inclusion exceeding 0.10% leads to deterioration of surface properties such as an increase in the amount of inclusions due to the formation of alumina. For this reason, Al was limited to the range of 0.02 to 0.10%. In addition, Preferably it is 0.05% or less.
　Ｎ：０．００５％未満
　Ｎは、固溶して鋼の強度増加に寄与し、比例限度を増加させる傾向を有するとともに、多量に含有するとスラブの熱間割れを発生させ、スラブの表面性状を悪化させる傾向を有する元素であり、本発明ではできるだけ低減することが望ましいが、０．００５％未満であれば許容できる。このため、Ｎは０．００５％未満に限定した。 N: Less than 0.005% N is a solid solution that contributes to increasing the strength of the steel and has a tendency to increase the proportional limit. When it is contained in a large amount, it causes hot cracking of the slab, and the surface properties of the slab Although it is an element which has a tendency to deteriorate and it is desirable to reduce it as much as possible in the present invention, it is acceptable if it is less than 0.005%. For this reason, N was limited to less than 0.005%.
　上記した成分が基本の成分であるが、基本の組成に加えてさらに、必要に応じて、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を選択して含有できる。
　Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上
　Ｔｉ、Ｎｂ、Ｂ、Ｃｒ、Ｍｏはいずれも、窒化物および／または炭化物を形成し、耐時効性を劣化させる固溶Ｃ，Ｎの減少に寄与する元素であり、必要に応じて選択して１種または２種以上含有できる。このような効果を得るためには、Ｔｉ：０．００５％以上、Ｎｂ：０．０１０％以上、Ｂ：０．０００３％以上、Ｃｒ：０．１％以上、Ｍｏ：０．１％以上、をそれぞれ含有することが望ましいが、Ｔｉ：０．０８％、Ｎｂ：０．０３０％、Ｂ：０．００３０％、Ｃｒ：１．０％、Ｍｏ：１．０％を、それぞれ超える含有は、析出物の増加や、焼入れ性の向上を介して低温変態相の増加等を促進し、鋼を硬質化させ延性を低下させる。このため、含有する場合には、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％の範囲にそれぞれ限定することが好ましい。 The above-mentioned components are basic components. In addition to the basic composition, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0. One or more selected from 0003 to 0.0030%, Cr: 0.1 to 1.0%, and Mo: 0.1 to 1.0% can be selected and contained.
Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0003 to 0.0030%, Cr: 0.1 to 1.0%, Mo: 0.1 to One or more selected from 1.0% Ti, Nb, B, Cr, and Mo all form solid solutions C and N that form nitrides and / or carbides and degrade aging resistance. It is an element that contributes to a decrease in the amount of N, and it can be selected as necessary and can be contained in one or more. In order to obtain such an effect, Ti: 0.005% or more, Nb: 0.010% or more, B: 0.0003% or more, Cr: 0.1% or more, Mo: 0.1% or more, It is desirable to contain Ti: 0.08%, Nb: 0.030%, B: 0.0030%, Cr: 1.0%, Mo: 1.0%, It promotes the increase of low temperature transformation phase through the increase of precipitates and the improvement of hardenability, hardens the steel and lowers the ductility. Therefore, when contained, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0003 to 0.0030%, Cr: 0.1 to 1.%. It is preferable to limit to 0% and Mo: 0.1 to 1.0%, respectively.
　上記した成分以外の残部は、Ｆｅおよび不可避的不純物からなる。
　また、本発明薄鋼板は、上記した組成を有し、さらに、平均結晶粒径：５~３０μｍのフェライト相を主体とする組織を有する。ここでいう「主体とする」とは、組織全体に対する体積率で９５％以上、好ましくは９８％以上、より好ましくは１００％である場合をいう。主体とする相以外の第二相は、セメンタイトやパーライト、ベイナイト等である。第二相は、体積率で５％以下とする。第二相が５％を超えて多くなると、鋼板が硬質化し、成形性（加工性）が低下する。 The balance other than the components described above consists of Fe and inevitable impurities.
The thin steel sheet of the present invention has the above-described composition and further has a structure mainly composed of a ferrite phase having an average crystal grain size of 5 to 30 μm. As used herein, “mainly” refers to a case where the volume ratio with respect to the entire tissue is 95% or more, preferably 98% or more, more preferably 100%. The second phase other than the main phase is cementite, pearlite, bainite, or the like. The second phase has a volume ratio of 5% or less. When the amount of the second phase exceeds 5%, the steel plate becomes hard and formability (workability) decreases.
　また、フェライト相の平均結晶粒径が５μｍ未満では、結晶粒界が多くなることから、調質圧延時の歪が、とくに粒界三重点に集中し、転位がタンダル化しやすくなるため、比例限度が増加する傾向となる。一方、フェライト相の平均結晶粒径が３０μｍを超えて結晶粒が粗大化すると、プレス成形時に、オレンジピールと称される凹凸が顕著となり、部材の表面性状が低下するとともに、比例限度の低減に必要な可動転位を、粒界近傍に導入することが困難となる。このようなことから、フェライト相の平均結晶粒径は５~３０μｍに限定した。 In addition, when the average crystal grain size of the ferrite phase is less than 5 μm, the grain boundaries increase, so the strain during temper rolling is concentrated especially at the triple boundary of the grain boundaries, and the dislocations tend to become tandals. Tend to increase. On the other hand, when the average crystal grain size of the ferrite phase exceeds 30 μm and the crystal grains become coarse, unevenness called orange peel becomes prominent at the time of press molding, the surface property of the member is lowered, and the proportional limit is reduced. It becomes difficult to introduce necessary movable dislocations near the grain boundaries. For this reason, the average crystal grain size of the ferrite phase is limited to 5 to 30 μm.
　さらに、本発明冷延薄鋼板は、上記した組成と上記した組織を有する薄鋼板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用した調質圧延を施してなる薄鋼板である。調質圧延に使用する圧延ロールの表面粗さＲａが２．０μｍを超えて粗い場合には、調質圧延時に導入される歪が鋼板表層に集中し、板厚方向に均一な歪を導入できず、所望の比例限度の低減が得られない。このため、本発明では、上記した組成と上記した組織を有する薄鋼板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用した調質圧延を施すことにした。 Furthermore, the cold-rolled thin steel sheet of the present invention is a thin steel sheet obtained by subjecting a thin steel sheet having the above composition and the above structure to temper rolling using a rolling roll having a surface roughness Ra of 2.0 μm or less. When the surface roughness Ra of the rolling roll used for temper rolling is coarser than 2.0 μm, the strain introduced during temper rolling is concentrated on the surface layer of the steel sheet, and uniform strain can be introduced in the sheet thickness direction. In other words, the desired proportional limit cannot be reduced. For this reason, in this invention, it decided to perform the temper rolling which uses the rolling roll whose surface roughness Ra is 2.0 micrometers or less to the thin steel plate which has the above-mentioned composition and the above-mentioned structure.
　つぎに、本発明薄鋼板の好ましい製造方法について説明する。
　本発明薄鋼板の製造方法では、まず、鋼素材に熱延工程、冷延工程、さらに焼鈍工程を順次施して、冷延焼鈍板とする。
　使用する鋼素材は、上記した鋼板の組成と同様に、質量％で、Ｃ：０．１０％以下、Ｓｉ：０．０５％以下、Ｍｎ：０．１~１．０％、Ｐ：０．０５％以下、Ｓ：０．０２％以下、Ａｌ：０．０２~０．１０％、Ｎ：０．００５％未満を含み、あるいはさらに、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を含み、残部Ｆｅおよび不可避的不純物からなる組成を有する鋼素材とする。
　鋼素材の製造方法は、とくに限定する必要はないが、上記した組成の溶鋼を転炉等の常用の溶製方法で溶製し、連続鋳造法などの常用の鋳造方法でスラブ等の鋼素材とすることが好ましい。鋼素材の鋳造方法は、成分のマクロな偏析を防止すべく違続鋳造法とすることが望ましいが、造塊法、薄スラブ鋳造法によってもなんら問題はない。
　まず、上記した組成の鋼素材に常法に従い、熱延工程と、冷延工程とを順次施し冷延板とする。 Below, the preferable manufacturing method of this invention thin steel plate is demonstrated.
In the method for producing a thin steel sheet of the present invention, first, a steel material is sequentially subjected to a hot rolling process, a cold rolling process, and an annealing process to obtain a cold rolled annealing sheet.
The steel material to be used is in mass%, C: 0.10% or less, Si: 0.05% or less, Mn: 0.1 to 1.0%, P: 0.0. 05% or less, S: 0.02% or less, Al: 0.02 to 0.10%, N: less than 0.005%, or Ti: 0.005 to 0.08%, Nb: 0 0.10 to 0.030%, B: 0.0003 to 0.0030%, Cr: 0.1 to 1.0%, Mo: 0.1 to 1.0% or one selected from 2 A steel material having a composition including more than seeds and the balance Fe and inevitable impurities is used.
The manufacturing method of the steel material is not particularly limited, but the molten steel having the above composition is melted by a conventional melting method such as a converter, and a steel material such as a slab by a conventional casting method such as a continuous casting method. It is preferable that The steel material casting method is desirably an intermittent casting method in order to prevent macro segregation of components, but there is no problem with the ingot casting method or the thin slab casting method.
First, according to a conventional method, a hot rolling process and a cold rolling process are sequentially performed on the steel material having the above composition to obtain a cold rolled sheet.
　本発明では、熱延工程は、鋼素材を加熱して、熱間圧延を施し、その後巻き取る工程を施し、所望の寸法形状の熱延板を製造できればよく、とくにその条件を限定する必要はない。
　ついで、得られた熱延板に冷延工程を施し、冷延板とする。冷延工程では、熱延板に酸洗を施し、ついで冷間圧延を施し冷延板とする。酸洗は、常用の酸洗方法がいずれも適用できる。また、冷間圧延は、所定の寸法形状の冷延板とすることができればよく、常用の冷間圧延条件がいずれも適用できる。 In the present invention, the hot rolling process is not limited as long as the steel material is heated, subjected to hot rolling, and then subjected to a winding process to produce a hot-rolled sheet having a desired dimension and shape. Absent.
Next, the obtained hot-rolled sheet is subjected to a cold-rolling step to obtain a cold-rolled sheet. In the cold rolling process, the hot rolled sheet is pickled and then cold rolled to obtain a cold rolled sheet. For pickling, any conventional pickling method can be applied. Moreover, the cold rolling should just be made into the cold-rolled board of a predetermined dimension shape, and all the normal cold rolling conditions can be applied.
　ついで、得られた冷延板に焼鈍工程を施し、冷延焼鈍板とする。
　焼鈍工程は、冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で３０ｓ以上加熱したのち、５℃／ｓ以上の平均冷却速度で６００℃以下の温度まで冷却する焼鈍処理を施す工程とする。これにより、平均結晶粒径ｄ：５~３０μｍのフェライト相を主体とする組織を有する冷延焼鈍板とする。 Subsequently, the obtained cold-rolled sheet is subjected to an annealing step to obtain a cold-rolled annealed sheet.
The annealing process is a process in which the cold-rolled sheet is subjected to an annealing process of heating to a temperature of 600 ° C. or less at an average cooling rate of 5 ° C./s after heating the cold rolled sheet at a temperature in the range of 730 to 850 ° C. for 30 s or more. And Thus, a cold-rolled annealed plate having a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 μm is obtained.
　焼鈍温度が、７３０℃未満では、冷間圧延で加工されたフェライトの再結晶の完了が困難となるうえ、平均結晶粒径：５μｍ以上の粗大フェライト粒を確保できない。一方、焼鈍温度が、８５０℃を超えて高温となると、オーステナイトへの変態が進行し、冷却時に微細なフェライトに変態するか、あるいは低温変態相へ変態し、フェライト分率が小さくなる。このため、焼鈍温度は：７３０~８５０℃の範囲の温度に限定することが好ましい。なお、焼鈍温度での保持（加熱）時間は３０ｓ以上とすることが好ましい。保持（加熱）時間が３０ｓ未満では、再結晶が完了しないか、完了しても粒成長が抑制され、所望の粗大フェライト粒を確保できなくなる。なお、加熱時間の上限はとくに限定しないが、生産性の観点から概ね２００ｓ以下とすることが望ましい。 If the annealing temperature is less than 730 ° C., it is difficult to complete recrystallization of ferrite processed by cold rolling, and coarse ferrite grains having an average crystal grain size of 5 μm or more cannot be secured. On the other hand, when the annealing temperature is higher than 850 ° C., the transformation to austenite proceeds and transforms to fine ferrite during cooling, or transforms to a low temperature transformation phase, and the ferrite fraction decreases. Therefore, the annealing temperature is preferably limited to a temperature in the range of 730 to 850 ° C. The holding (heating) time at the annealing temperature is preferably 30 s or more. If the holding (heating) time is less than 30 s, recrystallization will not be completed, or even if it is completed, grain growth is suppressed, and desired coarse ferrite grains cannot be secured. The upper limit of the heating time is not particularly limited, but is preferably about 200 s or less from the viewpoint of productivity.
　また、焼鈍工程での焼鈍後の冷却は、焼鈍温度から、５℃／ｓ以上の平均冷却速度で６００℃以下まで冷却することが好ましい。焼鈍後の冷却速度が、平均で５℃／ｓ未満では、フェライト粒の成長が促進され、所望の粒径範囲のフェライト組織とすることができなくなる。一方、焼鈍後冷延速度の上限はとくに限定する必要はないが、３０℃／ｓを超える急速な冷却で急冷する場合には特別な冷却設備を必要とするため、３０℃／ｓ以下の冷却速度で冷却することが好ましい。なお、冷却停止温度が６００℃を超えて高温となると、その後の冷却で低温変態相が形成される恐れがある。このため、焼鈍後の冷却は５℃／ｓ以上の平均冷却速度で６００℃以下まで冷却することとした。なお、６００℃以下の冷却速度は特に規定する必要はない。 In addition, the cooling after annealing in the annealing step is preferably performed from the annealing temperature to 600 ° C. or less at an average cooling rate of 5 ° C./s or more. When the cooling rate after annealing is less than 5 ° C./s on average, the growth of ferrite grains is promoted, and a ferrite structure having a desired grain size range cannot be obtained. On the other hand, it is not necessary to limit the upper limit of the cold rolling rate after annealing, but special cooling equipment is required for rapid cooling with rapid cooling exceeding 30 ° C./s, so cooling at 30 ° C./s or less. It is preferable to cool at a rate. If the cooling stop temperature exceeds 600 ° C. and becomes high, a low temperature transformation phase may be formed by subsequent cooling. For this reason, cooling after annealing was decided to cool to 600 ° C. or lower at an average cooling rate of 5 ° C./s or higher. In addition, it is not necessary to prescribe | regulate the cooling rate below 600 degreeC in particular.
　なお、得られた薄冷延焼鈍板に、電気亜鉛めっき、化成処理膜を形成してもよい。
　また、本発明では、上記した焼鈍工程に代えて、前記冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で焼鈍して、５℃／ｓ以上の平均冷却速度で６００℃以下の温度まで冷却し、溶融亜鉛めっきを施す焼鈍−溶融亜鉛めっき処理工程としてもよい。焼鈍−溶融亜鉛めっき処理工程は、連続溶融亜鉛めっきラインを利用し、焼鈍後、通常の４８０℃近傍の溶融亜鉛めっき浴に、連続浸漬する溶融亜鉛めっき処理を行ってもよい。なお、さらに、溶融亜鉛めっき層を合金化溶融亜鉛めっき層とする、めっき層の合金化処理工程を施してもよい。合金化処理は常法に従い５００℃以上６００℃未満の温度域に再加熱する処理とすればよい。 In addition, you may form electrogalvanization and a chemical conversion treatment film in the obtained thin cold-rolled annealing board.
In the present invention, instead of the above-described annealing step, the cold-rolled sheet is annealed at a temperature in the range of 730 to 850 ° C., and the average cooling rate of 5 ° C./s or more is 600 ° C. or less. It is good also as an annealing-hot galvanization process process which cools to temperature and performs hot dip galvanization. In the annealing-hot dip galvanizing treatment step, a hot dip galvanizing treatment may be performed by continuously dipping in a normal hot dip galvanizing bath near 480 ° C. using a continuous hot dip galvanizing line. Furthermore, a plating layer alloying treatment step may be performed in which the hot dip galvanized layer is an alloyed hot dip galvanized layer. The alloying treatment may be a reheating treatment in a temperature range of 500 ° C. or higher and lower than 600 ° C. according to a conventional method.
　このような熱延工程、冷延工程、焼鈍工程あるいは焼鈍−溶融亜鉛めっき処理工程、を経た冷延焼鈍板（めっき板）は、平均結晶粒径が５μｍ以上３０μｍ以下であるフェライト相を主体とする組織を有する冷延焼鈍板（めっき板）となる。なお、得られた冷延焼鈍板（めっき板）に、さらに、化成処理膜を形成してもよい。
　本発明では、冷延焼鈍板（めっき板）に、ついで、表面粗さＲａが２．０μｍ以下の圧延ロールを使用して調質圧延を施す。 A cold-rolled annealed plate (plated plate) that has undergone such a hot-rolling step, a cold-rolling step, an annealing step, or an annealing-hot-dip galvanizing treatment step is mainly composed of a ferrite phase having an average crystal grain size of 5 μm to 30 μm. It becomes a cold-rolled annealed plate (plated plate) having a texture to be formed. In addition, you may form a chemical conversion treatment film in the obtained cold-rolled annealing board (plating board) further.
In the present invention, the cold-rolled annealed plate (plated plate) is then subjected to temper rolling using a rolling roll having a surface roughness Ra of 2.0 μm or less.
　使用する圧延ロールの表面粗さＲａが２．０μｍを超えて粗くなると、図４に示すように、１５０ＭＰａ以下の比例限度を安定して確保できなくなる。使用する圧延ロールの表面粗さＲａの下限はとくに限定する必要はないが、使用する圧延ロールの表面粗さＲａが小さくなると、得られる鋼板の表面粗さも小さくなり、鋼板の摩擦抵抗が小さくなりすぎて、コイル状に巻き取った際に、コイルに巻きずれが生じて潰れやすくなる。このため、使用する圧延ロールの表面粗さＲａは０．２μｍ以上とすることが好ましい。なお、表面粗さＲａは、ＪＩＳ　Ｂ　０６０１−２００１の規定に準拠して測定した値を用いるものとする。 When the surface roughness Ra of the rolling roll to be used exceeds 2.0 μm, the proportional limit of 150 MPa or less cannot be stably secured as shown in FIG. The lower limit of the surface roughness Ra of the rolling roll to be used is not particularly limited. However, when the surface roughness Ra of the rolling roll to be used is reduced, the surface roughness of the obtained steel sheet is also reduced, and the frictional resistance of the steel sheet is reduced. Thus, when the coil is wound up, the coil is easily wound and crushed easily. For this reason, it is preferable that surface roughness Ra of the rolling roll to be used shall be 0.2 micrometer or more. In addition, the surface roughness Ra shall use the value measured based on prescription | regulation of JISB0601-2001.
　さらに、調質圧延における伸び率（調質圧延伸び率）Ｒ（％）は、被圧延材である冷延焼鈍板の平均結晶粒径をｄ（μｍ）とすると、（０．０５~０．２０）ｄとするのが良い。その理由は次の通りである。調質圧延を施すことにより、可動転位が導入され、比例限度が低減する。しかし、調質圧延により導入される可動転位は粒界近傍に導入されやすいため、所望の比例限度の低減に必要な可動転位を有効に粒界近傍に導入するには、フェライト粒径が大きいほど、調質圧延伸び率を大きくする必要がある。すなわち、フェライト平均粒径ｄ（μｍ）に応じて、調質圧延伸び率Ｒ（％）を調整することが肝要となる。調質圧延済み鋼板の比例限度（ＭＰａ）とＲ／ｄとの関係を図５に示す。なお、図５は、フェライト平均結晶粒径ｄが５~２０μｍの鋼板を用い、表面粗さＲａが０．２~１．８μｍの圧延ロールを使用して調質圧延した結果である。図５から、Ｒ／ｄが０．０５~０．２０の間で鋼板の比例限度が１５０ＭＰａ以下となることがわかる。 Further, the elongation ratio (temper rolling elongation ratio) R (%) in temper rolling is (0.05 to 0. 0), where d (μm) is the average crystal grain size of the cold-rolled annealed sheet as the material to be rolled. 20) It is good to set it as d. The reason is as follows. By applying temper rolling, movable dislocations are introduced and the proportional limit is reduced. However, movable dislocations introduced by temper rolling are likely to be introduced in the vicinity of grain boundaries. Therefore, in order to effectively introduce movable dislocations necessary for reducing the desired proportional limit to the vicinity of grain boundaries, the larger the ferrite grain size, It is necessary to increase the temper rolling elongation. That is, it is important to adjust the temper rolling elongation rate R (%) according to the ferrite average particle diameter d (μm). FIG. 5 shows the relationship between the proportional limit (MPa) of the temper-rolled steel sheet and R / d. FIG. 5 shows the result of temper rolling using a steel sheet having an average ferrite grain size d of 5 to 20 μm and a rolling roll having a surface roughness Ra of 0.2 to 1.8 μm. FIG. 5 shows that the proportional limit of the steel sheet is 150 MPa or less when R / d is between 0.05 and 0.20.
　調質圧延伸び率Ｒ（％）が、０．０５ｄ未満では、調質圧延の圧下量が不足し、所望の可動転位を導入できず、所望の低い比例限度を確保できない。一方、０．２０ｄを超えて圧下量が多くなると、導入された転位がタングル化し、比例限度低減に有効に寄与する可動転位が不足し、所望の低い比例限度を確保できなくなる。このようなことから、調質圧延伸び率Ｒ（％）は、フェライト平均結晶粒径ｄに対応して、（０．０５~０．２０）ｄの範囲に限定した。 If the temper rolling elongation rate R (%) is less than 0.05 d, the rolling amount of the temper rolling is insufficient, the desired movable dislocation cannot be introduced, and the desired low proportional limit cannot be ensured. On the other hand, when the amount of reduction exceeds 0.20d, the introduced dislocations are tangled, and the movable dislocation that effectively contributes to the reduction of the proportional limit is insufficient, and a desired low proportional limit cannot be secured. For this reason, the temper rolling elongation rate R (%) was limited to the range of (0.05-0.20) d corresponding to the ferrite average crystal grain size d.
　以下、実施例に基づいて、さらに本発明について説明する。 Hereinafter, the present invention will be further described based on examples.
　表１に示す組成の鋼素材に、１２００℃に加熱し、最終パスの出側温度を９００℃とする熱間圧延を施し、５５０℃で巻取り、板厚：２．６ｍｍの薄熱延板とする熱延工程を施した。得られた薄熱延板に、酸洗を施したのち、冷間圧延を施し、板厚０．８ｍｍの冷延板とする冷延工程を施した。ついで、得られた冷延板に、表２に示す焼鈍温度、保持時間、および冷却速度の条件で焼鈍処理を行う焼鈍工程を施し、薄冷延焼鈍板とした。なお、冷却速度は焼鈍温度から６００℃までの平均とした。 A steel material having the composition shown in Table 1 is heated to 1200 ° C., subjected to hot rolling at a final pass exit temperature of 900 ° C., wound at 550 ° C., and a sheet thickness of 2.6 mm. A hot rolling process was applied. The obtained thin hot-rolled sheet was pickled and then cold-rolled to give a cold-rolled step of forming a cold-rolled sheet having a thickness of 0.8 mm. Subsequently, the obtained cold-rolled sheet was subjected to an annealing process in which annealing treatment was performed under the conditions of annealing temperature, holding time, and cooling rate shown in Table 2 to obtain a thin cold-rolled annealed sheet. The cooling rate was an average from the annealing temperature to 600 ° C.
　一部の鋼板では、焼鈍処理に代えて、表２に示す条件で、焼鈍−溶融亜鉛めっき処理工程を施した。焼鈍−溶融亜鉛めっき処理工程では焼鈍処理に引続いて、めっき浴の温度：４８０℃の溶融亜鉛めっき浴に連続的に浸漬する溶融亜鉛めっき処理を施した。なお、一部の鋼板には、溶融亜鉛めっき処理後、表２に示す温度で合金化処理を施した。 Some steel sheets were subjected to an annealing-hot dip galvanizing process under the conditions shown in Table 2 instead of the annealing process. In the annealing-hot dip galvanizing treatment step, a hot dip galvanizing treatment in which the plating bath was continuously immersed in a hot dip galvanizing bath at a temperature of 480 ° C. was performed following the annealing treatment. Some steel sheets were subjected to alloying treatment at the temperatures shown in Table 2 after the hot dip galvanizing treatment.
　得られた薄冷延焼鈍板（薄めっき板）から、圧延方向に平行な断面が観察面となるように組織観察用試験片を採取し、研磨し、ナイタール腐食して、フェライト相の平均結晶粒径、組織分率を求めた。フェライト相の平均結晶粒径は、光学顕微鏡（倍率：１００倍）を用いて、２００×２００μｍの領域について、切断法により、求めた。また、フェライト相の組織分率は、光学顕微鏡（倍率：１００倍）を用いて、２００×２００μｍの領域について２枚撮像し、画像解析装置を用いて算出した。なお、フェライト以外の第二相についても観察した。組織観察結果を表２に併記して示す。 From the thin cold-rolled annealed plate (thin-plated plate), a specimen for observing the structure was collected so that the cross section parallel to the rolling direction becomes the observation surface, polished, and subjected to nital corrosion, and the average crystal of the ferrite phase The particle size and the texture fraction were determined. The average crystal grain size of the ferrite phase was determined by a cutting method for an area of 200 × 200 μm using an optical microscope (magnification: 100 times). In addition, the structure fraction of the ferrite phase was calculated using an image analysis apparatus by capturing two images of a 200 × 200 μm region using an optical microscope (magnification: 100 times). The second phase other than ferrite was also observed. The structure observation results are also shown in Table 2.
　ついで、得られた冷延焼鈍板（めっき板）に、表２に示す表面粗さＲａ（μｍ）の圧延ロールを使用して、表２に示す調質圧延伸び率Ｒ（％）で調質圧延を施した。圧延ロールの表面粗さＲａは、ＪＩＳ　Ｂ　０６０１−２００１の規定に準拠して測定した。なお、溶融亜鉛めっき処理を施さない一部の鋼板では、調質圧延後に電気亜鉛めっき処理を施した。
　調質圧延済み薄鋼板（薄めっき鋼板）から、試験方向が圧延方向となるように、ＪＩＳ５号試験片（ＧＬ：５０ｍｍ）を採取し、ＪＩＳ　Ｚ　２２４１の規定に準拠して引張試験を行い、引張特性（降伏強さＹＳ、引張強さＴＳ、伸びＥｌ）を求めた。また、得られた薄鋼板から、試験方向が圧延方向となるように、ＪＩＳ５号試験片を採取し、引張試験を実施して、比例限度を求めた。
比例限度は、平行部両面に歪ゲージ（ゲージ長さ：５ｍｍ）に貼付した引張試験片を用いて、引張速度：１ｍｍ／ｍｉｎで引張試験し、応力−歪曲線の傾き（Δσ／Δε）と応力（σ）との関係から、図３に示す要領で、求めた。 Next, the obtained cold-rolled annealed plate (plated plate) was tempered with a temper rolling elongation R (%) shown in Table 2 using a rolling roll having a surface roughness Ra (μm) shown in Table 2. Rolled. The surface roughness Ra of the rolling roll was measured in accordance with the provisions of JIS B 0601-2001. In addition, in some steel plates not subjected to hot dip galvanizing treatment, electrogalvanizing treatment was performed after temper rolling.
A JIS No. 5 test piece (GL: 50 mm) is sampled from a temper-rolled thin steel sheet (thin-plated steel sheet) so that the test direction is the rolling direction, and a tensile test is performed in accordance with the provisions of JIS Z 2241. Tensile properties (yield strength YS, tensile strength TS, elongation El) were determined. Further, from the obtained thin steel sheet, a JIS No. 5 test piece was sampled so that the test direction was the rolling direction, and a tensile test was performed to obtain a proportional limit.
The proportional limit is determined by performing a tensile test at a tensile speed of 1 mm / min using a tensile test piece affixed to strain gauges (gauge length: 5 mm) on both sides of the parallel portion, and the slope of the stress-strain curve (Δσ / Δε). It calculated | required in the way shown in FIG. 3 from the relationship with stress ((sigma)).
　なお、調質圧延済み薄鋼板についても、組織観察をしたが、冷延焼鈍板（めっき板）と変わらない組織を有していることを確認した。得られた結果を表３に示す。 In addition, although the structure of the temper-rolled thin steel sheet was also observed, it was confirmed that it had a structure that was not different from that of a cold-rolled annealed sheet (plated sheet). The obtained results are shown in Table 3.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003
　本発明例はいずれも、平均結晶粒径：５~３０μｍのフェライト相を主体とする組織を有し、１５０ＭＰａ以下の低い比例限度を有する薄鋼板となっている。一方、本発明の範囲を外れる比較例は、比例限度が１５０ＭＰａを超えている。 All of the examples of the present invention are thin steel sheets having a structure mainly composed of a ferrite phase having an average crystal grain size of 5 to 30 μm and a low proportional limit of 150 MPa or less. On the other hand, in the comparative example outside the scope of the present invention, the proportional limit exceeds 150 MPa.

Claims (7)

  1. 　質量％で、
    Ｃ　：０．１０％以下、　　　　　　　Ｓｉ：０．０５％以下、
    Ｍｎ：０．１~１．０％、　　　　　　Ｐ　：０．０５％以下、
    Ｓ　：０．０２％以下、　　　　　　　Ａｌ：０．０２~０．１０％、
    Ｎ　：０．００５％未満
    を含み、残部Ｆｅおよび不可避的不純物からなる組成と、平均結晶粒径ｄ：５~３０μｍのフェライト相を主体とする組織とを有する薄鋼板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用した調質圧延を施してなる薄鋼板であって、１５０ＭＰａ以下の比例限度を有することを特徴とする形状凍結性に優れた冷延薄鋼板。     % By mass
    C: 0.10% or less, Si: 0.05% or less,
    Mn: 0.1 to 1.0%, P: 0.05% or less,
    S: 0.02% or less, Al: 0.02-0.10%,
    N: a thin steel sheet containing less than 0.005%, the balance consisting of Fe and unavoidable impurities, and a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 μm has a surface roughness Ra. A cold-rolled thin steel sheet excellent in shape freezing property, which is a thin steel sheet subjected to temper rolling using a rolling roll of 2.0 µm or less and having a proportional limit of 150 MPa or less.
  2. 　前記組成に加えてさらに、質量％で、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を含有する組成とすることを特徴とする請求項１に記載の冷延薄鋼板。 In addition to the above composition, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0003 to 0.0030%, Cr: 0.1 to 2. The cold-rolled thin steel sheet according to claim 1, wherein the cold-rolled steel sheet has a composition containing one or more selected from 1.0% and Mo: 0.1 to 1.0%.
  3. 　請求項１または２に記載の冷延薄鋼板の少なくとも一方の表面に、溶融亜鉛めっき層、合金化溶融亜鉛めっき層、または電気亜鉛めっき層を形成してなることを特徴とする形状凍結性に優れた冷延薄鋼板。 A shape freezing property comprising a hot-dip galvanized layer, an alloyed hot-dip galvanized layer, or an electrogalvanized layer on at least one surface of the cold-rolled thin steel sheet according to claim 1 or 2. Excellent cold rolled steel sheet.
  4. 　鋼素材に熱延工程と、冷延工程とを順次施し冷延板とし、該冷延板に焼鈍工程を施し冷延焼鈍板とする冷延薄鋼板の製造方法において、前記鋼素材が、質量％で、
    Ｃ　：０．１０％以下、　　　　　　　　　　　Ｓｉ：０．０５％以下、
    Ｍｎ：０．１~１．０％、　　　　　　　　　　Ｐ　：０．０５％以下、
    Ｓ　：０．０２％以下、　　　　　　　　　　　Ａｌ：０．０２~０．１０％、
    Ｎ　：０．００５％未満
    を含み、残部Ｆｅおよび不可避的不純物からなる組成を有する鋼素材であり、
    前記焼鈍工程が、前記冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で３０ｓ以上加熱したのち、平均冷却速度：５℃／ｓ以上の冷却速度で６００℃以下の温度まで冷却する焼鈍処理を施し、平均結晶粒径ｄ：５~３０μｍのフェライト相を主体とする組織を有する冷延焼鈍板とする工程であり、
    前記焼鈍工程後に、前記冷延焼鈍板に、表面粗さＲａが２．０μｍ以下の圧延ロールを使用し、調質圧延伸び率（％）を、該冷延焼鈍板の平均結晶粒径ｄ（μｍ）に対応して、（０．０５~０．２０）ｄ（％）の範囲とする調質圧延を施し、比例限度が１５０ＭＰａ以下である冷延薄鋼板とすることを特徴とする、形状凍結性に優れた冷延薄鋼板の製造方法。     In the method of manufacturing a cold-rolled thin steel sheet, a steel sheet is subjected to a hot-rolling process and a cold-rolling process to form a cold-rolled sheet, and the cold-rolled sheet is subjected to an annealing process to form a cold-rolled annealed sheet. %so,
    C: 0.10% or less, Si: 0.05% or less,
    Mn: 0.1 to 1.0%, P: 0.05% or less,
    S: 0.02% or less, Al: 0.02-0.10%,
    N: steel material containing less than 0.005%, having a composition consisting of the remainder Fe and inevitable impurities,
    In the annealing step, the cold-rolled sheet is heated to an annealing temperature of 730 to 850 ° C. for 30 s or more, and then cooled to a temperature of 600 ° C. or less at an average cooling rate of 5 ° C./s or more. An annealing treatment is performed to form a cold-rolled annealing plate having a structure mainly composed of a ferrite phase having an average crystal grain size d: 5 to 30 μm,
    After the annealing step, a rolling roll having a surface roughness Ra of 2.0 μm or less is used for the cold-rolled annealed plate, and the temper rolling elongation (%) is determined by the average grain size d ( in accordance with (μm), a temper rolling in the range of (0.05-0.20) d (%) is applied to form a cold-rolled steel sheet having a proportional limit of 150 MPa or less. A method for producing a cold-rolled thin steel sheet having excellent freezing properties.
  5. 　前記焼鈍工程に代えて、前記冷延板に、焼鈍温度：７３０~８５０℃の範囲の温度で焼鈍して、５℃／ｓ以上の平均冷却速度で６００℃以下の温度まで冷却し、溶融亜鉛めっきを施す焼鈍−溶融亜鉛めっき処理工程とすることを特徴とする請求項４に記載の冷延薄鋼板の製造方法。 Instead of the annealing step, the cold rolled sheet is annealed at a temperature in the range of 730 to 850 ° C., cooled to a temperature of 600 ° C. or less at an average cooling rate of 5 ° C./s or more, and molten zinc The method for producing a cold-rolled thin steel sheet according to claim 4, wherein the annealing-hot dip galvanizing process is performed.
  6. 　前記焼鈍−溶融亜鉛めっき処理工程を経たのち、さらに溶融亜鉛めっきを合金化処理する合金化処理工程を施すことを特徴とする請求項５に記載の冷延薄鋼板の製造方法。 6. The method for producing a cold-rolled thin steel sheet according to claim 5, wherein after the annealing-hot dip galvanizing treatment step, an alloying treatment step of alloying the hot dip galvanizing is performed.
  7. 　前記鋼素材の組成に加えてさらに、質量％で、Ｔｉ：０．００５~０．０８％、Ｎｂ：０．０１０~０．０３０％、Ｂ：０．０００３~０．００３０％、Ｃｒ：０．１~１．０％、Ｍｏ：０．１~１．０％のうちから選ばれた１種または２種以上を含有する組成とすることを特徴とする請求項４ないし６のいずれかに記載の冷延薄鋼板の製造方法。 In addition to the composition of the steel material, further, by mass, Ti: 0.005 to 0.08%, Nb: 0.010 to 0.030%, B: 0.0003 to 0.0030%, Cr: 0 7. A composition containing one or more selected from 1 to 1.0% and Mo: 0.1 to 1.0%. The manufacturing method of the cold-rolled thin steel plate of description.
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