Classifications

• • 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
• • 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
  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • 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
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
• • 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
  • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
• • 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 high strength cold rolled steel sheet with formability and weldability that is suitably used for structures such as railway vehicles, automobiles, and ships.
• the present invention relates to a high strength cold rolled steel sheet having a tensile strength TS of 440 MPa or more and a method for manufacturing the same.
• Patent Documents 1 and 2 disclose cold rolled steel sheets with excellent formability. In the cold rolled steel sheets, resistance to cold-work embrittlement is improved by further adding B to the IF steel to which Ti or Nb is added.
• Patent Document 3 discloses a deep-drawing steel sheet with excellent brazing property obtained by further adding Ni to the IF steel to which Ti or Nb is added.
• an automotive steel sheet having higher strength has been developed in terms of weight reduction of a car body and crash safety of automobiles. Furthermore, a tailor-welded-blank made by combining two or more steel sheets having different thicknesses and characteristics through welding has been used as an automotive steel sheet to reduce the numbers of steps and dies. Therefore, there has been a growing demand for a high strength steel sheet with excellent formability and weldability, particularly a high strength cold rolled steel sheet having a TS of 440 MPa or more.
• Patent Document 4 discloses a method for manufacturing a tailor-welded-blank by welding steel sheets having different thicknesses through plasma welding that is performed with low equipment cost, at high speed, and without using a welding metal. In that method, a weld defect called humping bead is prevented by adjusting the C amount of the thicker steel sheet to 0.1% or more by mass or by adjusting the Si amount to 0.8% or more by mass.
• an object of the present invention is to achieve high speed welding by improving a steel sheet.
• an object of the present invention is to provide a high strength cold rolled steel sheet with excellent weldability in which humping bead is not formed by performing plasma welding at high speed and that has a TS of 440 MPa or more, which does not deteriorate the formability of a tailor-welded-blank.
• Another object of the present invention is to provide a method for manufacturing the high strength cold rolled steel sheet.
• the inventors of the present invention discovered the following findings after their investigation about the formability and weldability of a high strength cold rolled steel sheet in which humping bead is not formed by performing plasma welding at high speed and that has a TS of 440 MPa or more, which does not deteriorate the formability of a tailor-welded-blank.
• the present invention provides a high strength cold rolled steel sheet that is excellent in weldability and has a TS of 440 MPa or more, including a composition including C: 0.0005 to 0.005%, Si: 0.1 to 1.0%, Mn: 1 to 2.5%, P: 0.01 to 0.2%, S: 0.015% or less, sol. Al: 0.05% or less, N: 0.007% or less, Ti: 0.01 to 0.1%, B: 0.0005 to 0.0020%, Cu: 0.05 to 0.5%, and Ni: 0.03 to 0.5% by mass with the balance Fe and incidental impurities; and a microstructure constituted by a ferrite single phase.
• the composition preferably further includes 0: 0.0025 to 0.0080% by mass or at least one of Se: 0.0005 to 0.01% and Te: 0.0005 to 0.01% by mass.
• the high strength cold rolled steel sheet of the present invention can be manufactured by a method including the steps of hot-rolling a slab having the composition described above, coiling at a coiling temperature of 680°C or less, pickling, cold-rolling at a reduction ratio of 40% or more, and performing recrystallization annealing at 700 to 850°C.
• a high strength cold rolled steel sheet with excellent weldability in which humping bead is not formed by performing plasma welding at high speed and that has a TS of 440 MPa or more, which does not deteriorate the formability of a tailor-welded-blank can be manufactured. Furthermore, the high strength cold rolled steel sheet of the present invention with excellent formability is suitably used for not only automobile components but also electric device components and the like.
• % denotes the amount of elements expressed as percent by mass unless specified.
• the C amount is less than 0.0005%, a heavy burden is placed on decarbonization refining at a steelmaking stage, which increases the costs due to, for example, vacuum degassing.
• the C amount is more than 0.005%, the formability is deteriorated.
• the C amount is in the range of 0.0005 to 0.005%, and is preferably 0.003% or less.
• Si is an element that is effective for imparting higher strength to steel. To achieve such an effect, the Si amount needs to be 0.1% or more. However, a Si amount of more than 1.0% causes embrittlement of ferrite, which impairs the strength-ductility balance. Thus, the Si amount is in the range of 0.1 to 1.0%, and is preferably 0.7% or less.
• Mn is an element that is effective for imparting higher strength to steel. To achieve such an effect, the Mn amount needs to be 1% or more. However, a Mn amount of more than 2.5% facilitates centerline segregation in a slab and deteriorates the formability of end products. Thus, the Mn amount is in the range of 1 to 2.5%. To prevent hot brittleness due to FeS formation, Mn is combined with solid solution S in the steel to form MnS. In this case, assuming that the Mn amount is [Mn] and the S amount is [S], it is preferable to satisfy ([Mn]/55)/([S]/32) > 100.
• the P amount is an element that is effective for imparting higher strength to steel. To achieve such an effect, the P amount needs to be 0.01% or more. However, a P amount of more than 0.2% not only may cause grain boundary fracture in an HAZ or deteriorates low temperature toughness of a base metal or a welded portion, but also deteriorates an anti-crash property due to grain boundary segregation. Thus, the P amount is in the range of 0.01 to 0.2%.
• a S amount of more than 0.015% deteriorates low temperature toughness of a base metal or a welded portion as with P.
• the S amount is 0.015% or less, and a smaller amount is preferable.
• sol. Al 0.05% or less
• Al is normally used as a deoxidizing element at a steelmaking stage. Since the 0 amount is controlled within a specific range in the present invention, the sol. Al amount is 0.05% or less. A sol. Al amount of more than 0.05% is not preferable because the formability is deteriorated due to a large amount of Al 2 O 3 and inclusions may cause weld cracking. Thus, the sol. Al amount is 0.05% or less.
• a N amount of more than 0.007% deteriorates the formability and anti-aging property.
• the N amount is 0.007% or less, and a smaller amount is preferable.
• Ti improves the formability and anti-aging property by forming a precipitate with C or N.
• the Ti amount needs to be 0.01% or more.
• a Ti amount of more than 0.1% increases an alloy cost.
• the Ti amount is in the range of 0.01 to 0.1%.
• the B amount needs to be 0.0005% or more.
• a B amount of more than 0.0020% facilitates weld cracking.
• the B amount is in the range of 0.0005 to 0.0020%.
• Cu is an element that is effective for imparting higher strength without deteriorating formability and for preventing the formation of humping bead during high speed plasma welding.
• the effects are increased when Cu coexists with O controlled within the range described below in the steel.
• the Cu amount needs to be 0.05% or more.
• the Cu amount is in the range of 0.05 to 0.5%.
• the reason why the formation of humping bead during high speed plasma welding can be prevented when Cu coexists with 0 is uncertain, but it is believed that the viscosity of the steel melted during welding is optimized, which improves the flowability of molten steel.
• Ni amount is [Ni] and the Cu amount is [Cu], it is preferable to satisfy 0.25 ⁇ [Cu] ⁇ [Ni] ⁇ 0.75 ⁇ [Cu].
• the formation of humping bead during high speed plasma welding can be further suppressed when 0 coexists with Cu. It is believed that the viscosity and surface tension of the molten steel during welding is further optimized when O coexists with Cu. To achieve such an effect, the 0 amount in the steel needs to be 0.0025% or more, preferably 0.0040% or more. However, an 0 amount of more than 0.0080% saturates the effect, increases the cost for treating a slab surface due to a large number of blowholes of a continuous casting slab, and deteriorates the formability of the steel because of an increase in the number of inclusions.
• Se and Te optimize the viscosity and surface tension of the molten steel during welding and prevent the formation of humping bead during high speed plasma welding when they coexist with Cu.
• the Se or Te amount needs to be 0.0005% or more.
• a Se or Te amount of more than 0.01% saturates the effects.
• a microstructure constituted by a ferrite single phase is required.
• the ferrite single phase herein may be either a polygonal ferrite phase or a bainitic ferrite phase or a mixture thereof.
• the average grain diameter of the ferrite phase is preferably 50 ⁇ m or less.
• the high strength cold rolled steel sheet of the present invention can be manufactured by a method including the steps of hot-rolling a slab having the composition described above, coiling at a coiling temperature of 680°C or less, pickling, cold-rolling at a reduction ratio of 40% or more, and performing recrystallization annealing at 700 to 850°C.
• the coiling temperature is more than 680°C, a chemical compound of P and Fe, Ti, or the like is easily formed, which impedes the development of a ⁇ 111 ⁇ texture that is preferred for deep-drawing formability when cold-rolling and annealing performed later.
• the coiling temperature is 680°C or less, preferably 650°C or less.
• the reduction ratio is 40% or more. In terms of improvement in formability and, particularly, deep drawability, the reduction ratio is preferably 50% or more.
• the annealing temperature needs to be 700°C or more for recrystallization. However, when the annealing temperature exceeds 850°C, ferrite grains are coarsened, which decreases strength or deteriorates surface quality. Thus, the recrystallization annealing temperature is in the range of 700 to 850°C. To sufficiently perform recrystallization, a steel sheet is preferably held at 750°C or more for 30 seconds or longer.
• Manufacturing conditions of typical methods can be applied to other manufacturing conditions of the present invention.
• steel is smelted in a converter or an electric furnace to form a slab through continuous casting.
• the slab may be rolled after heat treatment, directly rolled without heat treatment, or rolled after short-time heat treatment.
• Hot rolling may be performed at a finishing temperature equal to or higher than the Ar 3 transformation temperature as with typical procedures.
• the recrystallization annealing can be performed by box annealing or continuous annealing. After the annealing, skin pass rolling may be performed, for example, for the purpose of the adjustment of surface roughness and the planarization of a plate shape. Subsequently, surface treatments such as a chemical conversion treatment and a plating treatment may be conducted.
• Each of steel Nos. 1 to 7 having an elemental composition of 0:002% C-0.2% Si-1.8% Mn-0.05% P-0.005% S-0.02% sol. Al-0.003% N-0.04% Ti-0.0010% B with Cu, 0, and Se shown in Table 1 was smelted by vacuum melting, heated at 1200°C for 1 hour, and then rough-rolled to make a sheet bar having a thickness of 35 mm.
• the sheet bar was heated at 1250°C for 1 hour and finish-rolled such that the finish rolling entering temperature was 900°C after seven passes. Subsequently, heat treatment corresponding to coiling was performed at 580°C for 1 hour to obtain a hot rolled steel sheet having a thickness of 4 mm.
• the hot rolled steel sheet was descaled through pickling and cold-rolled at a reduction ratio of 60% to obtain a cold rolled steel sheet having a thickness of 1.6 mm. Recrystallization annealing in which heating is conducted at 830°C for 180 sec and cooling is then conducted at a cooling rate of 10°C/sec was performed using a salt bath. After pickling was performed in order to remove the salt attached to the surface of the steel sheet, skin pass rolling was conducted at an elongation percentage of 0.5%.
• the maximum speed that can achieve welding without forming humping bead was about 0.2 to 0.4 m/min.
• humping bead was not formed at a high welding speed of 1 m/min in the sample (steel No. 3) containing Cu according to the present invention and at a high welding speed of 1 m/min or more in the samples (steel Nos. 4 to 7) further containing 0 and Se. Accordingly, the samples of the present invention have high speed plasma weldability.
• Each of steel Nos. A to F having compositions shown in Table 2 was smelted to obtain a slab through continuous casting.
• the slab was heated at 1200°C and then finish-rolled at a finishing temperature of 900°C.
• the slab was coiled at a coiling temperature of 580°C to obtain hot rolled steel sheets having thicknesses of 6 mm and 4 mm.
• the hot rolled steel sheets were pickled and cold-rolled at a reduction ratio of 60% to obtain cold rolled steel sheets having thicknesses of 2.4 mm and 1.6 mm.
• Continuous annealing was performed at an annealing temperature of 830°C and skin pass rolling was conducted at an elongation percentage of 0.5%.
• Table 3 shows the results.
• the steel sheets having compositions of invention examples exhibit a TS of 440 MPa or more and are excellent in formability.
• humping bead is not formed during high speed plasma welding.
• Table 2 Steel No. Composition (% by mass) Note C Si Mn P S sol.Al N Ti B Cu Ni O (Mn/55)/(S/32) Other A 0.0015 0.2 1.9 0.079 0.007 0.050 0.0016 0.037 0.001 0.09 0.05 ⁇ 0.002 158 - within the scope of the invention B 0.0025 0.2 2.0 0.075 0.007 0.050 0.0015 0.035 0.0015 0.12 0.05 0.005 166 - within the scope of the invention C 0.0015 0.7 1.2 0.030 0.006 0.030 0.0020 0.061 0.0015 0.06 0.035 0.003 116 Se:0.005 within the scope of the invention D 0.0012 0.6 1.3 0.036 0.008 0.026 0.0007 0.032 0.0006

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• 2008
  • 2008-08-05 JP JP2008201735A patent/JP5391606B2/ja active Active
• 2009
  • 2009-07-24 CA CA2731843A patent/CA2731843C/en not_active Expired - Fee Related
  • 2009-07-24 WO PCT/JP2009/063622 patent/WO2010016430A1/ja active Application Filing
  • 2009-07-24 MX MX2011000901A patent/MX2011000901A/es active IP Right Grant
  • 2009-07-24 KR KR1020117002627A patent/KR101335826B1/ko active IP Right Grant
  • 2009-07-24 US US13/057,573 patent/US20110290383A1/en not_active Abandoned
  • 2009-07-24 CN CN200980131036.0A patent/CN102119234B/zh active Active
  • 2009-07-24 EP EP09804914.1A patent/EP2312007B1/en active Active
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