CN100363523C - Ferritic stainless steel sheet excellent in formability and its manufacturing method - Google Patents

Ferritic stainless steel sheet excellent in formability and its manufacturing method Download PDF

Info

Publication number
CN100363523C
CN100363523C CNB2004100462473A CN200410046247A CN100363523C CN 100363523 C CN100363523 C CN 100363523C CN B2004100462473 A CNB2004100462473 A CN B2004100462473A CN 200410046247 A CN200410046247 A CN 200410046247A CN 100363523 C CN100363523 C CN 100363523C
Authority
CN
China
Prior art keywords
quality
stainless steel
annealing
hot
steel sheet
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
CNB2004100462473A
Other languages
Chinese (zh)
Other versions
CN1572895A (en
Inventor
秀岛保利
富村宏纪
平松直人
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Nippon Steel Nisshin Co Ltd
Nippon Steel Stainless Steel Corp
Original Assignee
Nisshin Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nisshin Steel Co Ltd filed Critical Nisshin Steel Co Ltd
Publication of CN1572895A publication Critical patent/CN1572895A/en
Application granted granted Critical
Publication of CN100363523C publication Critical patent/CN100363523C/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • 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
    • C21D8/0405—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 of ferrous alloys
    • 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
    • C21D8/0468—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 between cold rolling steps
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C21D8/0463—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 following hot 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
    • C21D8/0447—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

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

A ferritic stainless steel sheet has a composition of C up to 0.02 mass %, Si up to 0.8 mass %, Mn up to 1.5 mass %, P up to 0.050 mass %, S up to 0.01 mass %, 8.0-35.0 mass % of Cr, N up to 0.05 mass %, 0.05-0.40 mass % of Ti and 0.10-0.50 mass % of Nb with a product of (%Tix%N) less than 0.005. Precipitates of 0.15 mu m or more in particle size except TiN are distributed in a steel matrix at a rate of 5000-50000/mm<2>. The steel sheet is manufactured by hot-rolling a slab at a finish-temperature of 800 DEG C or lower, annealing the hot-rolled steel sheet at 450-1080 DEG C, cold-rolling the hot-rolled steel sheet in accompaniment with intermediate-annealing at a temperature within a range of from (a recrystallization-finishing temperature -100 DEG C) to (a recrystallization-finishing temperature) and then finish-annealing the cold-rolled steel sheet at 1080 DEG C or lower.

Description

Ferrite stainless steel and production method thereof with excellent formability
Technical field
The present invention relates to a kind of ferrite stainless steel, but its press forming is a kind of not such as the circularity of difference and the predetermined profile of deflection, but and post forming be a kind of final profile with good hot extrude performance, also relate to its manufacture method.
Background technology
Ferritic stainless steel is represented with SUS430 or SUS430LX, has been used for various different field so far already, for example, durable consumer goods, this is that they have good solidity to corrosion and more cheap owing to compare with austenitic stainless steel (it contain Ni be a kind of expensive element).Along with its application and development, it is more and more stricter that a kind of ferrite stainless steel of press forming is that a kind of condition of product design becomes.For instance, the steel plate of press forming often carries out post forming to carry out hole flanging.Along with its application and development, a kind of new ferrite stainless steel need be provided strongly, it has very good formability with respect to traditional ferrite stainless steel, even and if can be configured as the product design that does not also have defective under severe condition.
For the shaping of ferrite stainless steel, many reports had been arranged already.Representative improvement is to add Ti and Nb simultaneously, with stable C of dissolved and the N that exists as carbonitride.And JP2000-192199A has provided the distribution of magnesium inclusion (it is effective for resisting wrinkling) in the ferritic stainless steel that contains Ti and Nb.JP8-26436B has provided the combination of the hot-rolled condition that is added with Ti and Nb, and they are designed to be used for improve as the blue gram of formability exponential Ford (Lankford) value (r).
Just the shape freezing and the post forming of shaping stainless steel plate (it will be used for being configured as final profile) are the same with anti-wrinkling property with Lankford value (r), also are important factors.
Ferrite stainless steel has poor formability usually with respect to austenite stainless steel plate.Especially, it obviously reduces the thickness that is in first shaped state, and the thickness reduction is anisotropic.Consequently, when described ferrite stainless steel press forming was cylindrical shape, it is poorer that dimensional precision such as circularity become along with the molding condition of harshness.The thickness deviation that is in first shaped state can cause the serious degradation of secondary formability such as hole flanging (hole-extruding).
Can keep high dimensional precision (for example for ferrite stainless steel at the press forming state, circularity, planeness and warp resistance) and the situation of post forming, cheap ferrite stainless steel substitutes expensive austenite stainless steel plate as parts or element, from the molding condition of harshness, austenite is haveed no alternative but and will be used.
Summary of the invention
The object of the present invention is to provide a kind of ferrite stainless steel, be dispersed in that sedimentary particle size and distribution in the steel matrix are improved its dimensional precision and in the post forming performance of press forming state by control.
The present invention proposes a kind of new ferrite stainless steel, it contains 0.02 quality % or lower C, 0.8 quality % or lower Si, 1.5 quality % or lower Mn, 0.050 quality % or lower P, 0.01 quality % or lower S, 8.0-35.0 the Cr of quality %, 0.05 quality % or lower N, 0.05-0.40 the Ti of quality %, 0.10-0.50 the Nb of quality %, non-essential 0.5 quality % or the lower Ni of being selected from, 3.0 quality % or lower Mo, 2.0 quality % or lower Cu, 0.3 quality % or lower V, 0.3 quality % or lower Zr, 0.3 one or more among quality % or lower Al and 0.0100 quality % or the lower B, with surplus except inevitable impurity be Fe, and (product of %Ti * %N) is less than 0.005.It is that 0.15 μ m or bigger throw out are by 5000-50000/mm that its structure is defined as except that TiN particle size 2Ratio distribute.
Described ferrite stainless steel is made as follows:
A kind of molten steel with predetermined composition is cast into a slab.Is steel plate with described slab 800 ℃ or lower terminal temperature hot rolling, and anneals at 450-1080 ℃.Hot-rolled steel sheet after the annealing carries out pickling, and carries out cold rollingly, is attended by at least one process annealing step simultaneously, its temperature range in (recrystallize terminal temperature-100 ℃) between (recrystallize terminal temperature).Described cold-rolled steel sheet carries out final annealing at last under 1080 ℃ or lower temperature.
Described hot-rolled steel sheet can carry out pack annealing, continues one hour or the shorter scheduled time.Described process annealing and described final annealing can carry out in continuous annealing furnace, continue one minute or shorter time.
Description of drawings
Fig. 1 is the synoptic diagram that is used for explaining a kind of steel plate circularity that is formed by multiple deck press cylinder ground.
Embodiment
In order (for example to improve dimensional precision, circularity, planeness and deflection), the inventor studies creating conditions of ferrite stainless steel from different aspects and checks, is subjected to the influence of TiN and other sedimentary shape and distribution in the as-annealed condition with having been found that the circularity of press forming steel plate and post forming certain degree.Based on these discoveries, the contriver infers that some target capabilitiess can be composed and be added on the ferrite stainless steel by suitably controlling described sedimentary shape and distribution.Forming described throw out is shape and the distribution that is suitable for this purpose, can by in ferritic stainless steel to add Ti and Nb and to make described ferritic stainless steel carry out optimal heat machinery and handle and realize greater than stablizing C and N numerical value as carbonitride metering ratio.
Sedimentary shape and distribution are explained as follows the influence of press formability and dimensional precision:
Because the adding of Ti and Nb, C in the ferritic stainless steel and N mainly are sedimentary with carbonitride form.Described sedimentary carbonitride except TiN is being cold-rolled to the manufacturing processed of final annealing from annealing hot-rolled steel sheet process, and major part all forms very fine particle again.The recrystallize particulate that this fine granular can allow to have the clog-free effect of a certain orientation is grown with preponderating, when manufactured steel plates when recrystallize is carried out in annealing, will form anisotropic particulate mixed structure.This anisotropy causes in first shaping steel plate process the strain concentrating along a certain direction, thereby makes the press formability and the dimensional precision variation of described steel plate.
Blocking action in the recrystallization annealing process (pinning action) according to having the sedimentary distribution of particle size greater than a certain numerical value, can be estimated.This blocking action can suppress directed particulate growth or be grown to the thickness grain, so just can improve the anisotropy and the dimensional precision of the steel plate of press forming.This blocking action is to the influence of press formability and dimensional precision, can be that 0.15 μ m or bigger throw out are by 5000-50000/mm by particle size except that TiN 2Ratio distribute and show, it will obtain confirming in embodiment subsequently.
In described throw out, TiN is disadvantageous for press formability and dimensional precision.In fact, contain that (product of %Ti * %N) can break when the press forming state greater than 0.005 steel plate.At the super initial point of these disruptive, can observe thick TiN particle (they have been grown to cubic shape).Observations shows, strain concentrating is on cube summit and cause fine fisssure in compacting process.In circumgranular strain concentrating of described TiN and formation fine fisssure, also be unfavorable for the hole flanging in the post forming step.
Ferrite stainless steel of the present invention contains the alloying constituent of predetermined proportion, and is as follows:
[0.02 quality % or lower C]
C is converted into the carbide that helps the unordered growth of recrystallize ferrite particulate in the final annealing step, still, because its hardening effect can reduce the formability of steel plate.The precipitation of carbide also can cause poor erosion resistance.In this, consider formability and erosion resistance, C content should be controlled at alap level, i.e. 0.02 quality % or lower.In order to improve post forming, described C content preferably is reduced to 0.015 quality % or lower.However, still, reduce described C content, need a long refining operation, thereby improved the steel production cost to extremely low level.Therefore, the lower limit of described C content preferably is defined as 0.001 quality %.The qualification of this lower limit also can guarantee the effect of carbide to the unordered growth of recrystallize ferrite particulate in the final annealing step.
[0.8 quality % or lower Si]
Si is a kind of alloying constituent (it is to add in the steel production process as oxygen scavenger), and still, it also has strong solution hardening effect.Greater than the excessive Si of 0.8 quality %, can make the steel plate sclerosis unfriendly, thereby cause it to have poor ductility.Consider ductility and post forming, the upper limit of Si content preferably is defined as 0.5 quality %.
[1.5 quality % or lower Mn]
Because its solution hardening effect is weaker than Si, Mn can not make the steel plate sclerosis significantly.However, can cause in the steel production process that greater than the excessive Mn of 1.5 quality % manganese smog emits, thereby cause the throughput o of difference
[0.050 quality % or lower P]
P is deleterious for hot workability, so its upper limit is defined as 0.050 quality %.
[0.01 quality % or lower S]
S is a kind of harmful element, and its is understood in the particulate edge separation, and the particulate edge is become fragile.These shortcomings can be by control S content to 0.01 quality % or lower being inhibited.
[Cr of 8.0-35.0 quality %]
In order to guarantee stainless erosion resistance, Cr content is controlled at 8.0 quality % or bigger.However, still, along with the raising of Cr content, stainless toughness and formability meeting variation are so the upper limit of described Cr content is defined as 35.0 quality %.Described Cr content preferably is controlled at 20.0 quality % or lower, with further its ductility and the post forming of improving.
[0.05 quality % or lower N]
N is converted into the nitride that helps the unordered growth of recrystallize ferrite particulate in the final annealing step, and still, it has hardening effect.Because excessive N can reduce the ductility of steel plate, so N content should be controlled at alap level, i.e. 0.05 quality % or lower.In order further to improve its ductility and post forming, described N content preferably is controlled at 0.02 quality % or lower.However, reduce described N content, need a long refining operation, thereby improved the steel production cost to extremely low level.Therefore, the lower limit of described N content preferably is defined as 0.001 quality %.The qualification of this lower limit also can guarantee the effect of nitride to the unordered growth of recrystallize ferrite particulate in the final annealing step.
[Ti of 0.05-0.40 quality %]
Ti is a kind of alloying constituent, and it can stablize C and N as carbonitride, helps formability and erosion resistance.This class effect is that 0.05 quality % or bigger time performance are very obvious at Ti content.However, can cause the cost raising of steel greater than the excessive Ti of 0.40 quality %, and can cause the surface imperfection that is derived from titanium inclusion.
[0.10-0.50 quality % or lower Nb]
Nb (it has the effect identical with Ti for stablizing C with N) is 0.15 μ m or bigger niobium inclusion for precipitation particle size except that TiN, is a kind of important composition.Described niobium inclusion may be by carbide and Fe 2Nb forms.In order to precipitate this class niobium inclusion, 0.10 quality % or more Nb are essential.However, can cause too much precipitation greater than the excessive Nb of 0.50 quality %, and improve the recrystallization temperature of ferritic stainless steel unfriendly.
[0.5 quality % or lower Ni]
With regard to the toughness and the erosion resistance of hot-rolled steel sheet, Ni is a kind of optional elements.But, add excessive N i and can improve raw materials cost, and can make the steel plate sclerosis, so the upper limit of Ni content is defined as 0.5 quality %.
[3.0 quality % or lower Mo]
With regard to erosion resistance, Mo is a kind of optional elements, still, is disadvantageous greater than the excessive Mo of 3.0 quality % for hot workability.
[2.0 quality % or lower Cu]
Cu is a kind of optional elements, and in the steel production process, it often is present in the stainless steel next by residue.Because excessive Cu can cause the reduction of poor toughness and hot workability, so Cu content is controlled at and is at most 2.0 quality %.
[0.3 quality % or lower V or Zr]
V and Zr are optional elements.V can fix free C and be present in the steel matrix as carbide, help formability, and Zr can catch free O, helps formability and toughness.However, consider throughput, add excessive V or Zr and must avoid.On this meaning, the upper limit of V or Zr is defined as 0.3 quality %.
[0.3 quality % or lower Al]
Al is a kind of optional elements, and it adds among the steel production process as reductor.However, the increase of non-metallic inclusion be can cause, thereby the toughness and the surface imperfection of difference caused greater than the excessive Al of 0.3 quality %.
[0.0100 quality % or lower B]
B is a kind of optional elements, and it can stablize N, and can improve stainless erosion resistance and formability.The effect of B is clearly at 0.0010 quality % or when bigger, still, is disadvantageous greater than the excessive B of 0.0100 quality % for hot workability and weldability.
Except above-mentioned element, Ca, Mg, Co, REM (rare earth metal) etc. also may be present in the residue in the steel production process.This dvielement is for the circularity of deep-draw steel plate or the not significantly influence of dimensional precision of press forming steel plate, unless they are to exist with ratio extraordinary.
[(％Ti×％N)＜0.005]
Along with (%Ti * %N) increase of numerical value, TiN are grown to thick particle or form bunch.Thick TiN particle or bunch meeting promotion strained gathering in first forming process, thus cause forming fine fisssure in the previous stage of tensile.Thick TiN particle or bunch this deleterious effect, can (%Ti * %N) be eliminated to the numerical value that is lower than 0.005, and it will obtain confirming in embodiment subsequently by control.
[particle size is that 0.15 μ m or bigger throw out are by 5000-50000/mm except that TiN 2Ratio distribute]
Particle size is that 0.15 μ m or bigger carbide and nitrides precipitate thing have blocking action, can suppress directed particulate growth and be grown to the thickness grain, thereby can improve the anisotropy of stainless steel plate, the circularity of circular column draft state and the dimensional precision of press forming state.
Throw out is carbide and the nitride of Ti and Nb, this (Laves) phase of pressgang and composition thereof.TiN particle (they precipitate with cubic shape) is to get rid of outside the throw out favourable to press formability and dimensional precision, and this is because cube TiN particle may strain in its vertex set, and serves as the starting point of fine fisssure.Particle size is that 0.15 μ m or bigger throw out are by 5000-50000/mm except that TiN 2Ratio distribute, can guarantee press formability and the favourable blocking action of dimensional precision to the press forming steel disc, it will obtain confirming in embodiment subsequently.
Described throw out is to a kind of press formability of press forming steel disc and the influence of dimensional precision, is 0.15 μ m or is significantly when bigger in particle size, and become bigger along with the increase of described particle size.However, particle size is unwelcome greater than the first lees of 1.0 μ m, and this is because this coarse particles can promote the formation of strained gathering and fine fisssure in compacting process, thereby causes poor shape freezing.Described sedimentary blocking action is at 5000/mm 2Or be significantly during bigger distribution proportion, still, greater than 50000/mm 2But sedimentary excessive distribution will reduce the ductility and the deep drawing quality of steel plate.Excessive distribution will improve the recrystallization temperature of steel plate unfriendly, thereby makes steel plate be difficult to be annealed to the recrystallize state.
For controlling sedimentary shape and the necessary working condition that distributes, will become more clear from following explanation.
[carrying out hot rolling] 800 ℃ or lower terminal temperature
In relatively low terminal temperature ferrite stainless steel is carried out hot rolling, to bring out sedimentary nuclear site, it will be distributed among the steel plate of final annealing.Ferrite particulate edge and internal strain at hot-rolled state serve as described nuclear site.In order to bring out described nuclear site as much as possible, the hot rolled terminal temperature is determined at 800 ℃ or lower.
[the hot rolled steel plate being annealed] at 450-1080 ℃
By at 450-1080 ℃ the hot rolled steel plate being annealed, the throw out in the hot-rolled steel sheet is adjusted to a kind of described sedimentary shape that is suitable for controlling, and they will be distributed among the final steel plate, be 0.15 μ m or bigger particle size.If described annealing temperature is lower than 450 ℃, then will be difficult to form effective throw out.On the contrary, if described hot rolling copper coin heats in the temperature that is higher than 1080 ℃, then the described throw out except that TiN will be dissolved among the steel matrix with being out of favour again.
Do not grow into coarse particles in order suitably to control sedimentary distribution number, described annealing was finished in one hour.
[carrying out process annealing] in (recrystallize terminal temperature-100 ℃) to the temperature range between (recrystallize terminal temperature)
In cold-rolled process, in order to suppress the dissolving again of described throw out (they form by the described hot-rolled steel sheet of annealing), steel plate is annealed at relatively lower temp.Only being lower than the process annealing temperature of recrystallize terminal temperature, is preferred for separating de-stress (it is introduced among the described steel plate owing to cold rolling).To between (recrystallize terminal temperature), then described steel plate can be softened as long as described annealing temperature remains on (recrystallize terminal temperature-100 ℃), and dissolving again of throw out, no matter also remaining also do not have the rolling structure of recrystallize.
For fear of described sedimentary dissolving again, estimate the ability of conventional continuous annealing furnace, the described process annealing stage finished in 1 minute.
[under 1080 ℃ or lower temperature, carrying out final annealing]
By final annealing, rolling structure can be eliminated.But the temperature that is higher than 1080 ℃ is disadvantageous for mass production not only, and can promote describedly sedimentaryly to dissolve again and grow into the thickness grain, thereby causes the toughness of difference.
Estimate the ability of conventional continuous annealing furnace, described final annealing was finished in one minute.
Further feature of the present invention will clearly be illustrated by following embodiment, though scope of the present invention is not limited to these embodiment.
Embodiment 1 (infrastest)
The contriver has furtherd investigate under the following conditions TiN (it often is deposited in the ferrite stainless steel matrix) effect and throw out shape effects to the dimensional precision of press forming steel disc and the effect of post forming.
Fusing polylith iron and steel in an experimental furnace, and be cast into slab, wherein every block of iron and steel all is adjusted to and has following composition: except Fe and unavoidable impurities, contain Cr, the A1 of 0.04 quality % of Cu, 16.50 quality % of S, 0.05 quality % of P, 0.0005 quality % of Mn, 0.030 quality % of Si, 0.25 quality % of C, the 0.40 quality % of 0.007 quality %, condition is that Nb, Ti and N content change between 0.02-0.30 quality %, 0.05-0.30 quality % and 0.005-0.035 quality % respectively.
Table 1 has provided described Nb, Ti and N content and (the sum of products recrystallize terminal temperature of %Ti * %N).
Table 1:Nb, Ti and N content (quality %) and (%Ti * %N) and recrystallize terminal temperature T Rf(℃)
The iron and steel numbering Nb Ti N ％Ti×％N T rf
1 0.2 0.06 0.005 0.0003 910
2 0.06 0.035 0.0021 900
3 0.2 0.01 0.0020 930
4 0.2 0.02 0.0040 940
5 0.3 0.01 0.0030 955
6 0.3 0.02 0.0060 950
7 0.3 0.035 0.0105 940
8 0.02 0.2 0.01 0.0020 910
9 0.3 0.2 0.01 0.0020 960
The numeral of underscore is the numerical value outside the present invention.
The hot rolling under 750 ℃ terminal temperature of each slab is the thickness of 4mm.
Hot-rolled steel sheet numbering 1-7 is that the cold rolling thickness of 2mm that is was followed in pickling 800 ℃ of annealing 60 seconds.Be accompanied by in the temperature of (recrystallize terminal temperature-50 ℃) and carried out process annealing 60 seconds, continuing described steel plate cold rolling is the final thickness of 0.5mm.Described cold-rolled steel sheet carries out final annealing at 1000 ℃, continues 60 seconds.
Described hot-rolled steel sheet numbering 8 and 9 is annealed, pickling and cold rollingly subsequently be the thickness of 2mm.Described steel plate carries out process annealing and continues the cold rolling final thickness of 0.5mm that is.Described cold-rolled steel sheet is carried out final annealing.Table 2 has provided the condition of annealing hot-rolled steel sheet, process annealing and final annealing.
Table 2: the condition of annealing hot-rolled steel sheet, process annealing and final annealing
Plating numerals The annealing numbering The annealing hot-rolled steel sheet Process annealing Final annealing
(℃) (second) (℃) (second) (℃) (second)
8 Y1 1090 60 950 60 950 60
Y2 700 60 850 60 950 60
Y3 700 28800 850 60 950 60
9 Y4 1100 60 950 60 1000 60
Y5 700 60 1000 60 1000 60
Y6 700 60 900 60 1000 60
Y7 750 1500 900 60 1000 60
Y8 700 3000 900 60 1000 60
Y9 700 28800 900 60 1000 60
[sedimentary distribution proportion and shape]
Test steel disc of sampling under potentiostatic condition, corrodes in the nonaqueous electrolytic solution of a kind of 10% methyl ethyl diketone-1% Tetramethylammonium chloride-methyl alcohol from each annealed sheet steel, and adopts scanning electronic microscope to observe, to study sedimentary distribution.In any 50 sites, the cross section parallel with rolling direction checked, measure each sedimentary maximum length, and it is decided to be particle size.
[dimensional precision of press forming steel disc]
Blank of sampling is cylindrical shape (as shown in Figure 1) by multiple deck press with its press forming from each annealed sheet steel.Adopting laser ranger, is the position of 5mm at distance flange section F, measures maximum radius and the minimum radius of column part C.Calculate the ratio of (maximum diameter-minimum diameter)/(minimum diameter), and with its circularity as evaluation press forming plate size precision.
[post forming]
Make the height of another test steel disc projection 10mm, be adopt one have shaft shoulder radius-of-curvature be 10mm, diameter be the stamping machine of 103mm and one to have shaft shoulder radius-of-curvature be that 8mm, diameter are the punch die of 105mm, realize under at the flange of test steel disc by a globule fixed condition.Take out the blank that diameter is 92mm from described projection test steel disc bottom, at described blank center by removing 10% aperture that to form a diameter be 10mm.Carry out the post forming property testing after the described blank as follows:
With described blank be fixed on one have shaft shoulder radius-of-curvature be 3mm, diameter be the flat primary drying press of 40mm and one to have shaft shoulder radius-of-curvature be that 3mm, diameter are between the punch die of 42mm, fix over against described die stamping mode with burr along described aperture.Described aperture is extruded flange by described stamping machine, and up to breaking at its edge, the flange of described blank is fixed by a globule simultaneously.Measure the diameter in described hole at the section start that breaks.According to the following equation: second reaming rate (%)=(flange bore dia-not flange bore dia)/(not flange bore dia) * 100 calculates the second reaming rate.
The gained result is as shown in table 3.It shows, and (product of %Ti * %N) is greater than in 0.005 compacting process of carrying out, and steel plate breaks.No matter working condition how, the Nb content of formation is lower than the steel plate of 0.02 quality %, has poor circularity.For the observations of the poor circularity steel plate of all having of steel plate and formation of breaking, prove that except that TiN particle size is that the throw out of 0.15 μ m only has a little to be distributed among the steel matrix.
On the other hand, along with the increase of described throw out (they are distributed in Nb content is among 0.3 quality % or the more steel matrix) number, linkage heat mechanical treatment condition, circularity improves.However, described sedimentary excessive distribution is inappropriate for circularity.
(product of %Ti * %N) is very inferior aspect post forming greater than 0.005 steel plate.The post forming of difference also shows on the steel plate with 0.02 quality %Nb.
The improvement of post forming (being hole flanging) is along with the increase of described throw out (they are distributed in Nb content is among 0.3 quality % or the more steel matrix) number obtains confirming.However, described sedimentary excessive distribution is inappropriate for post forming.
The dimensional precision of The above results proof press forming steel plate and post forming depend on that particle size is 0.15 μ m or bigger sedimentary distribution except that TiN.That is to say, make this class throw out by 5000-50000/mm 2The optimal heat machinery that the control of ratio distributes is handled, and is effective for dimensional precision and post forming.
Table 3: circularity and post forming and the relation of precipitate distribution except that TiN
Sample number into spectrum Plating numerals The annealing numbering The throw out number * (/mm 2) Circularity Post forming
1 1 - 12000 0.8 51
2 2 - 11000 1.6 52
3 3 - 12700 1.7 59
4 4 - 14200 2.2 53
5 5 - 13500 1.9 52
6 6 - 12500 Break 23
7 7 - 12300 Break 20
8 8 Y1 50 3.9 43
9 8 Y2 50 4.2 48
10 8 Y3 150 3.1 46
11 9 Y4 1000 3.2 42
12 9 Y5 1500 3.7 40
13 9 Y6 7000 2.2 62
14 9 Y7 32000 1.8 58
15 9 Y8 42000 1.9 52
16 9 Y9 80000 4.2 38
Throw out *: particle size is 0.15 μ m or bigger except that TiN.
Embodiment 2
Have and form polylith stainless steel as shown in table 4 and in vacuum oven, melt and be cast into slab.Steel A-H belongs to the present invention, and the composition of the discontented unabridged version invention of steel I-L limits.
Each slab hot rolling is the thickness of 4.0mm, annealing, pickling, and cold rolling be the thickness of 2mm.Described cold-rolled steel sheet carries out process annealing, and continuing cold rolling is the final thickness of 0.5mm, carries out final annealing afterwards.Table 5 has provided the hot rolling terminal temperature, the condition of anneal hot-rolled steel sheet, process annealing and final annealing.
Table 4: the chemical constitution of ferritic stainless steel (quality %)
The iron and steel kind C Si Mn P S Cr N Ti Nb Other Ti×N T rf
A 0.013 0.06 0.18 0.032 0.0002 13.93 0.007 0.18 0.13 Zr：0.21 Al：0.08
B 0.003 0.5 0.26 0.013 0.003 15.63 0.005 0.22 0.32 B：0.0072 Cu：1.22 0.0011 970
C 0.006 0.08 0.26 0.023 0.002 16.55 0.008 0.18 0.25 Al：0.08 B：0.0015 0.0014 960
D 0.008 0.08 0.36 0.022 0.001 17.3 0.009 0.14 0.25 Mo：1.02 0.0013 960
E 0.01 0.2 0.52 0.024 0.003 22 0.011 0.31 0.24 Mo：0.5 0.0034 990
F 0.008 0.16 0.36 0.009 0.004 9.8 0.009 0.2 0.22 0.0018 870
G 0.003 0.17 0.21 0.01 0.0005 32 0.005 0.12 0.2 V：0.08 0.0006 1020
H 0.006 0.1 0.17 0.027 0.001 16.52 0.011 0.15 0.25 B：0.0014 Al：0.016 Ni：0.1 0.0017 950
I 0.04 0.26 0.31 0.03 0.003 16.8 0.007 0.12 0.23 0.0008 950
J 0.008 0.2 0.31 0.02 0.002 18.3 0.008 0.1 0.04 0.0008 920
K 0.013 0.19 0.21 0.012 0.003 17.3 0.012 0.12 0.8 0.0014 1030
L 0.01 0.18 0.23 0.011 0.002 16.5 0.02 0.29 0.48 0.0058 1000
T RfBe the recrystallize terminal temperature (℃).
Table 5: the terminal temperature of hot rolling and processing steel plate
The iron and steel kind Sample number into spectrum Terminal temperature (℃) Annealing *1 Annealing *2 Annealing *3 Note
(℃) (second) (℃) (second) (℃) (second)
A A1 780 950 60 870 10 950 30 The invention example
A2 760 890 60 950 600 980 30 Comparative Examples
B B1 750 760 60 950 20 1000 5 The invention example
B2 830 760 60 950 20 1020 5 Comparative Examples
C C1 750 490 3600 950 30 1000 60 The invention example
C2 760 490 7200 950 30 1000 60 Comparative Examples
D D1 790 550 600 900 60 1000 20 The invention example
D2 740 550 600 900 60 1110 60 Comparative Examples
E E1 780 850 600 900 60 1040 60 The invention example
F F1 790 700 600 800 60 950 60 ″
G G1 780 750 3600 1000 60 1000 60 ″
H H1 760 700 60 900 60 1000 60 ″
H2 760 700 60 1000 60 1000 60 Comparative Examples
H3 760 1100 60 900 60 1000 60 ″
H4 760 700 60 900 60 1100 70 ″
I I1 780 890 20 920 30 980 60 ″
J J1 770 700 3600 880 60 980 60 ″
K K1 760 800 600 950 60 1050 60 ″
L L1 770 760 60 950 60 1050 60 ″
Annealing * 1Be the thermal treatment of hot-rolled steel sheet.
Annealing * 2It is the intermediate heat treatment in cold-rolled process.
Annealing * 3Be the final thermal treatment of cold-rolled steel sheet.
Adopt the method identical that each block plate is tested, to study the dimensional precision and the post forming of sedimentary shape and distribution and press forming steel plate with embodiment 1.
Result in the table 6 shows, particle size except TiN wherein is that 0.15 μ m or bigger throw out are with 5000-50000/mm 2Ratio be distributed in ferrite stainless steel in the steel matrix, being pressed and being shaped for having 2.5% or the good profile of lower circularity.
On the other hand, contrast steel plate (they satisfy composition condition of the present invention, but they are produced under inappropriate condition), embodiment numbers A2, B2, C2 and D2, and (sedimentary distribution number is in 5000-50000/mm except that TiN owing to its metallographic structure 2Outside) reason, they have poor dimensional precision and post forming when the press forming state.
In steel plate I, owing to existing excessive C to become really up to the mark, and in the process of press forming, break.In steel plate K, owing to existing excessive N b to become too firm, and in compacting process, break.(product of %Ti * %N) also breaks in compacting process greater than 0.005 steel plate L, and wherein, described breaking beginning near thick TiN particle.The insufficient steel plate J of Nb has poor circularity when press forming.
Can be understood by above-mentioned contrast, be 0.15 μ m or bigger sedimentary distribution by control particle size except that TiN, and ferrite stainless steel can press forming be the purpose profile with high dimensional accuracy and good post forming.
Table 6: the relation of circularity and post forming and precipitate distribution
The steel plate kind Sample number into spectrum The precipitate distribution number *(/mm 2) Circularity (%) Post forming (%) Note
A A1 7200 1.3 51 The invention example
A2 4500 2.7 48 Comparative Examples
B B1 12000 2.3 53 The invention example
B2 4600 3.6 49 Comparative Examples
C C1 23000 2 53 The invention example
C2 80000 2.9 44 Comparative Examples
D D1 16000 2.2 60 The invention example
D2 320 3.6 32 Comparative Examples
E E1 8000 0.9 50 The invention example
F F1 12000 0.8 51 ″
G G1 23000 2.2 50 ″
H H1 13000 0.8 68 ″
H2 100 2.9 48 Comparative Examples
H3 50 3.2 44 ″
H4 50 4 32 ″
I I1 12000 Break 12 ″
J J1 130 3.3 34 ″
K K1 78000 Break 22 ″
L L1 13000 Break 22 ″
*Throw out particle size except that TiN is 0.15 μ m or bigger.
According to above-mentioned the present invention, can be pressed and be shaped for having the ferrite stainless steel of high dimensional accuracy and good post forming, be to be that 0.15 μ m or bigger throw out are with 5000-50000/mm by particle size except that TiN 2Ratio be distributed in to have in the steel matrix that control forms and provide.Being suitable for the sedimentary shape of this class and the distribution of this purpose, is to realize by controlling the process annealing in hot rolling terminal temperature and annealing hot-rolled steel sheet, the cold-rolled process and the heat-treat condition of final annealing cold-rolled steel sheet suitably.By the ferritic stainless steel that this method is produced, in various different field, be very useful the element of the strict dimensional precision of those needs or the parts, for example, the sealing element that is used for Organnic electroluminescent device, precision stamping goods, receptor, utensil, the burner of stove, the oil filler pipe of tanks, motor casing, housing, sender unit cap, spray tube, thermostatic valve, bearing seal, flanges etc. can be used for substituting expensive austenite stainless steel plate.

Claims (4)

1. ferrite stainless steel, have following composition: the Nb of Ti, the 0.10-0.50 quality % of Cr, the 0.05 quality % of 0.02 quality % or lower C, 0.8 quality % or lower Si, 1.5 quality % or lower Mn, 0.050 quality % or lower P, 0.01 quality % or lower S, 8.0-35.0 quality % or lower N, 0.05-0.40 quality % and except unavoidable impurities surplus be Fe, and (product of %Ti * %N) is less than 0.005, and
Its structure is that 0.15 μ m or bigger throw out are by 5000-50000/mm for particle size except that TiN 2Ratio be distributed among the steel matrix.
2. according to the ferrite stainless steel of claim 1, also comprise one or more elements of from 0.5 quality % or lower Ni, 3.0 quality % or lower Mo, 2.0 quality % or lower Cu, 0.3 quality % or lower V, 0.3 quality % or lower Zr, 0.3 quality % or lower Al and 0.0100 quality % or lower B, selecting.
3. the production method of a ferrite stainless steel may further comprise the steps:
A kind of ferrite stainless steel base with following composition is provided: the Nb of Ti, the 0.10-0.50 quality % of Cr, the 0.05 quality % of 0.02 quality % or lower C, 0.8 quality % or lower Si, 1.5 quality % or lower Mn, 0.050 quality % or lower P, 0.01 quality % or lower S, 8.0-35.0 quality % or lower N, 0.05-0.40 quality % and except unavoidable impurities surplus be Fe, and (product of %Ti * %N) is less than 0.005;
800 ℃ or lower terminal temperature described slab is carried out hot rolling;
Temperature 450-1080 ℃ of scope is annealed to described hot-rolled stainless steel plate;
Hot-rolled steel sheet after the described annealing is carried out cold rolling, is attended by at least one process annealing step simultaneously, the temperature range of described process annealing than the temperature of low 100 ℃ of recrystallize terminal temperature between the recrystallize terminal temperature; With then
1080 ℃ or lower temperature described cold-rolled steel sheet is carried out final annealing.
4. according to the production method of claim 3, wherein the ferrite stainless steel base also comprises one or more elements of selecting from 0.5 quality % or lower Ni, 3.0 quality % or lower Mo, 2.0 quality % or lower Cu, 0.3 quality % or lower V, 0.3 quality % or lower Zr, 0.3 quality % or lower Al and 0.0100 quality % or lower B.
CNB2004100462473A 2003-06-04 2004-06-04 Ferritic stainless steel sheet excellent in formability and its manufacturing method Expired - Lifetime CN100363523C (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP159275/2003 2003-06-04
JP2003159275A JP3886933B2 (en) 2003-06-04 2003-06-04 Ferritic stainless steel sheet excellent in press formability and secondary workability and manufacturing method thereof
JP159275/03 2003-06-04

Publications (2)

Publication Number Publication Date
CN1572895A CN1572895A (en) 2005-02-02
CN100363523C true CN100363523C (en) 2008-01-23

Family

ID=33157175

Family Applications (1)

Application Number Title Priority Date Filing Date
CNB2004100462473A Expired - Lifetime CN100363523C (en) 2003-06-04 2004-06-04 Ferritic stainless steel sheet excellent in formability and its manufacturing method

Country Status (7)

Country Link
US (2) US20040244884A1 (en)
EP (1) EP1484424B1 (en)
JP (1) JP3886933B2 (en)
KR (1) KR100595383B1 (en)
CN (1) CN100363523C (en)
DE (1) DE602004028780D1 (en)
ES (1) ES2357303T3 (en)

Families Citing this family (32)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2006233251A (en) * 2005-02-23 2006-09-07 Nippon Steel & Sumikin Stainless Steel Corp Method for producing high purity ferritic stainless steel and product thereof
CN100385032C (en) * 2006-02-17 2008-04-30 山西太钢不锈钢股份有限公司 Middle content chromium copper, iron-containing antiseptic anticreas rustless steel sheet belt and its production method
KR20080110662A (en) 2006-05-09 2008-12-18 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 Stainless steel excellent in corrosion resistance, ferritic stainless steel excellent in crevice corrosion resistance and formability, and ferritic stainless steel excellent in crevice corrosion resistance
DK1882756T3 (en) * 2006-07-26 2012-03-05 Sandvik Intellectual Property Ferritic chrome steel
JP5297630B2 (en) * 2007-02-26 2013-09-25 新日鐵住金ステンレス株式会社 Ferritic stainless steel plate with excellent heat resistance
JP4998719B2 (en) * 2007-05-24 2012-08-15 Ｊｆｅスチール株式会社 Ferritic stainless steel sheet for water heaters excellent in punching processability and method for producing the same
WO2009025125A1 (en) * 2007-08-20 2009-02-26 Jfe Steel Corporation Ferritic stainless steel plate excellent in punchability and process for production of the same
CN101514431B (en) * 2008-02-21 2011-11-23 宝山钢铁股份有限公司 High-strength high-elongation Cr17 cold-rolled steel strip and method for manufacturing same
JP5420292B2 (en) * 2008-05-12 2014-02-19 日新製鋼株式会社 Ferritic stainless steel
JP5366498B2 (en) * 2008-10-17 2013-12-11 日新製鋼株式会社 Cu-plated ferritic stainless steel sheet and multi-turn steel pipe
CN101812641B (en) * 2009-02-25 2013-09-04 宝山钢铁股份有限公司 Ferrite stainless steel
JP4798298B2 (en) 2009-07-30 2011-10-19 Ｊｆｅスチール株式会社 Stainless steel for fuel cell separator with excellent conductivity and ductility and method for producing the same
JP5501795B2 (en) * 2010-02-24 2014-05-28 新日鐵住金ステンレス株式会社 Low-chromium stainless steel with excellent corrosion resistance in welds
CN101942609A (en) * 2010-08-09 2011-01-12 振石集团东方特钢股份有限公司 Ferrite stainless steel with low ductile-brittle transition temperature
CN101979166B (en) * 2010-09-20 2012-10-10 首钢总公司 Production method of low-yield-ratio micro-alloy pipeline steel hot-rolled coiled plate
JP5152387B2 (en) * 2010-10-14 2013-02-27 Ｊｆｅスチール株式会社 Ferritic stainless steel with excellent heat resistance and workability
CN102618790B (en) * 2012-03-26 2014-11-05 宝山钢铁股份有限公司 High-strength low-Cr ferrite stainless steel and manufacturing method thereof
JP5937861B2 (en) * 2012-03-27 2016-06-22 新日鐵住金ステンレス株式会社 Heat-resistant ferritic stainless steel sheet with excellent weldability
UA111115C2 (en) 2012-04-02 2016-03-25 Ейкей Стіл Пропертіс, Інк. cost effective ferritic stainless steel
CN103510013B (en) * 2013-09-29 2018-06-05 宝钢不锈钢有限公司 The stanniferous ferritic stainless steel and its manufacturing method of a kind of good wrinkle resistance
JP6541992B2 (en) * 2015-03-12 2019-07-10 日鉄ステンレス株式会社 Automotive parts and automotive fueling pipes excellent in puncture resistance utilizing painting and sacrificial corrosion protection effect
JP6598478B2 (en) * 2015-03-12 2019-10-30 日鉄ステンレス株式会社 Oil supply pipe for automobiles with excellent salt damage resistance and reduced external appearance deterioration
JP6005234B1 (en) * 2015-09-29 2016-10-12 日新製鋼株式会社 High-strength stainless steel sheet with excellent fatigue characteristics and method for producing the same
KR101835003B1 (en) 2016-09-28 2018-04-20 주식회사 포스코 Ferritic stainless steel for exhaust system heat exchanger having excellent sound absorption ability and method of manufacturing the same
JP6768929B2 (en) * 2017-03-29 2020-10-14 日鉄ステンレス株式会社 Ferritic stainless steel with excellent high-temperature wear resistance, manufacturing method of ferritic stainless steel sheet, exhaust parts, high-temperature sliding parts, and turbocharger parts
CN109136735A (en) * 2017-06-27 2019-01-04 宝钢不锈钢有限公司 Ferritic stainless steel and its manufacturing method with favorable forming property
KR102109898B1 (en) * 2018-06-26 2020-05-12 주식회사 포스코 LOW-Cr FERRITIC STAINLESS STEEL WITH EXCELLENT VIBRATION DAMPING PROPERTY AND MANUFACTURING METHOD THEREOF
WO2020084987A1 (en) * 2018-10-25 2020-04-30 Ｊｆｅスチール株式会社 Ferrite stainless hot-rolled-and-annealed steel sheet and production method for same
CN113227414B (en) * 2018-12-21 2023-08-11 日铁不锈钢株式会社 Cr-based stainless steel sheet excellent in hydrogen embrittlement resistance
JP7304715B2 (en) * 2019-03-04 2023-07-07 日鉄ステンレス株式会社 Ferritic stainless steel plate
CN113005269A (en) * 2021-02-20 2021-06-22 山西太钢不锈钢精密带钢有限公司 Production method of precipitation hardening stainless steel precision strip steel for precision electronic products
CN113502376A (en) * 2021-06-18 2021-10-15 鞍钢联众(广州)不锈钢有限公司 Method for improving secondary skin inclusion of titanium-containing stainless steel billet

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11236650A (en) * 1998-02-20 1999-08-31 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member excellent in workability, intergranular corrosion resistance and high temperature strength
JP2000192199A (en) * 1998-12-25 2000-07-11 Nippon Steel Corp Ferritic stainless steel excellent in ridging characteristic and workability in weld zone
US20030094217A1 (en) * 2001-10-31 2003-05-22 Kawasaki Steel Corporation Ferritic stainless steel sheet having excellent deep-drawability and brittle resistance to secondary processing and method for making the same

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5933645B2 (en) * 1976-10-15 1984-08-17 新日本製鐵株式会社 Manufacturing method of highly workable ferritic stainless steel sheet with less occurrence of ridging
JP3706428B2 (en) * 1996-03-15 2005-10-12 新日鐵住金ステンレス株式会社 Ferritic stainless steel for automotive exhaust system equipment
JP3601512B2 (en) * 2000-12-22 2004-12-15 Ｊｆｅスチール株式会社 Ferritic stainless steel sheet for fuel tank and fuel pipe and method for producing the same
US6786981B2 (en) * 2000-12-22 2004-09-07 Jfe Steel Corporation Ferritic stainless steel sheet for fuel tank and fuel pipe
EP1225242B1 (en) * 2001-01-18 2004-04-07 JFE Steel Corporation Ferritic stainless steel sheet with excellent workability and method for making the same
JP3932020B2 (en) * 2001-11-19 2007-06-20 日新製鋼株式会社 Ferritic stainless steel with excellent deep drawability and small in-plane anisotropy and method for producing the same

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11236650A (en) * 1998-02-20 1999-08-31 Kawasaki Steel Corp Ferritic stainless steel for engine exhaust member excellent in workability, intergranular corrosion resistance and high temperature strength
JP2000192199A (en) * 1998-12-25 2000-07-11 Nippon Steel Corp Ferritic stainless steel excellent in ridging characteristic and workability in weld zone
US20030094217A1 (en) * 2001-10-31 2003-05-22 Kawasaki Steel Corporation Ferritic stainless steel sheet having excellent deep-drawability and brittle resistance to secondary processing and method for making the same

Also Published As

Publication number Publication date
EP1484424A1 (en) 2004-12-08
DE602004028780D1 (en) 2010-10-07
US20090165905A1 (en) 2009-07-02
KR100595383B1 (en) 2006-06-30
KR20040104939A (en) 2004-12-13
CN1572895A (en) 2005-02-02
ES2357303T3 (en) 2011-04-25
JP2004360003A (en) 2004-12-24
EP1484424B1 (en) 2010-08-25
US20040244884A1 (en) 2004-12-09
JP3886933B2 (en) 2007-02-28

Similar Documents

Publication Publication Date Title
CN100363523C (en) Ferritic stainless steel sheet excellent in formability and its manufacturing method
US10450626B2 (en) High-strength hot-dip galvanized steel sheet excellent in formability and method of producing same
WO2009154235A1 (en) Steel for heat treatment
CN110168116B (en) Hot-stamped molded body and method for producing same
RU2643735C1 (en) Low-alloyed steel pipe for oil well
US20180066344A1 (en) Wire rod for use in bolts that has excellent acid pickling properties and resistance to delayed fracture after quenching and tempering, and bolt
KR20080079178A (en) The ferritic stainless steel plate having low orange peel and exhibiting excellent formability, and method for producing the same
EP2554706A1 (en) Hot-rolled steel sheet with high tensile strength and superior processability and method for producing same
EP3816316A1 (en) Ultrahigh-strength hot-rolled steel sheet and steel strip having good fatigue and reaming properties and manufacturing method therefor
KR100733017B1 (en) High strength cold rolled steel sheet and method for manufacturing the same
CN109923235B (en) Ultrahigh-strength steel sheet having excellent hole expansibility and yield ratio, and method for producing same
CN102725432B (en) Highly corrosion-resistant hot-rolled ferrite stainless steel sheet having excellent toughness
JP5308726B2 (en) Austenitic stainless steel sheet for press forming having a fine grain structure and method for producing the same
CN108138286A (en) Steel, the product of the steel making and its manufacturing method
KR20200100159A (en) Ferritic stainless steel sheet and its manufacturing method
CN112805398A (en) Austenitic stainless steel having excellent pipe expandability and age-crack resistance
KR100222080B1 (en) Fe-cr alloy exhibiting excellent riding resistance and surface characteristics
JP5073966B2 (en) Age-hardening ferritic stainless steel sheet and age-treated steel using the same
JP2003213376A (en) Ferritic stainless steel sheet having excellent secondary hole enlargementability and production method therefor
KR100756114B1 (en) Method for production of high strength thin steel sheet excellent in hole expansibility, ductility and chemical treatment characteristics
JP2020164956A (en) Ferritic stainless steel sheet and manufacturing method therefor
CN111549285B (en) Ultra-low carbon tin plate with excellent corrosion resistance and preparation method thereof
JP3886864B2 (en) Ferritic stainless steel cold-rolled annealed material excellent in secondary workability and manufacturing method thereof
JPH11106873A (en) Alloy for electron gun electrode
CN111902558A (en) Steel sheet for hot stamping

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
C14 Grant of patent or utility model
GR01 Patent grant
CP01 Change in the name or title of a patent holder
CP01 Change in the name or title of a patent holder

Address after: Tokyo, Japan

Patentee after: NISSHIN STEEL Co.,Ltd.

Address before: Tokyo, Japan

Patentee before: NISSHIN STEEL Co.,Ltd.

TR01 Transfer of patent right
TR01 Transfer of patent right

Effective date of registration: 20220316

Address after: Tokyo, Japan

Patentee after: NIPPON STEEL & SUMIKIN STAINLESS STEEL Corp.

Address before: Tokyo, Japan

Patentee before: NIPPON STEEL & SUMITOMO METAL Corp.

Effective date of registration: 20220316

Address after: Tokyo, Japan

Patentee after: NIPPON STEEL & SUMITOMO METAL Corp.

Address before: Tokyo, Japan

Patentee before: NISSHIN STEEL Co.,Ltd.

CX01 Expiry of patent term

Granted publication date: 20080123