CN107964632A - The excellent ferrite series stainless steel plate of molding processibility - Google Patents

The excellent ferrite series stainless steel plate of molding processibility Download PDF

Info

Publication number
CN107964632A
CN107964632A CN201711384153.0A CN201711384153A CN107964632A CN 107964632 A CN107964632 A CN 107964632A CN 201711384153 A CN201711384153 A CN 201711384153A CN 107964632 A CN107964632 A CN 107964632A
Authority
CN
China
Prior art keywords
less
stainless steel
steel plate
series stainless
cold
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.)
Granted
Application number
CN201711384153.0A
Other languages
Chinese (zh)
Other versions
CN107964632B (en
Inventor
寒川孝
太田裕树
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.)
JFE Steel Corp
JFE Engineering Corp
Original Assignee
NKK Corp
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
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=50340884&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=CN107964632(A) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by NKK Corp filed Critical NKK Corp
Publication of CN107964632A publication Critical patent/CN107964632A/en
Application granted granted Critical
Publication of CN107964632B publication Critical patent/CN107964632B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—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
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—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
    • C22C38/06—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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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

Abstract

The present invention, which provides, meets the excellent ferrite series stainless steel plate of the molding processibility of deep drawability and wrinkle resistance.The ferrite series stainless steel plate contains C in terms of quality %：0.010~0.070%, Si：Less than 1.00%, Mn：Less than 1.00%, P：Less than 0.040%, S：Less than 0.010%, Al：Less than 0.150%, Cr：14.00~20.00%, Ni：Less than 1.00%, N：0.010~0.060%, and then, contain V：0.005~0.100%, B：0.0001~0.0050% and meet V/B >=10, surplus is made of Fe and inevitable impurity.

Description

The excellent ferrite series stainless steel plate of molding processibility
The application is the 201380046801.5 (applying date of patent application：On September 6th, 2013, invention and created name：Shaping The ferrite series stainless steel plate of excellent in workability) divisional application.
Technical field
The present invention relates to be suitable for the purposes such as the kitchen appliance of building, household supplies, electrified product, automobile component Ferrite series stainless steel plate, more particularly to meets deep drawability and the molding processibility of wrinkle resistance (ridging resistance) Excellent ferrite series stainless steel plate.It should illustrate that the steel plate in the present invention includes steel band, steel plate, foil.
Background technology
Ferrite-group stainless steel be widely used in as the material of excellent corrosion resistance using household supplies, automobile component as The various industrial fields represented.The ferrite-group stainless steel is cheaper than the austenite stainless steel containing a large amount of Ni.But usually Poor in processability, such as when implementing processing and forming, easily produce and be referred to as corrugated surface defect, be not suitable for implementation deep drawing and add Work etc. forces the purposes of work.In addition, also there are intra-face anisotropy (the Δ r) of plastic strain ratio (r values) for ferrite-group stainless steel Also it is big and the problem of easily cause non-uniform deformation in deep-draw deep processing.Therefore, in order to further expand ferrite not The application range of rust steel plate, it is desirable to improve the r values of the index as deep drawability, reduce the intra-face anisotropy of plastic strain ratio (Δ r), and then improve wrinkle resistance.
For such requirement, such as Patent Document 1 discloses a kind of ferrite-group stainless steel of excellent in workability, its Contain C：0.03~0.08%, Si：Less than 0.4%, Mn：Less than 0.5%, P：Less than 0.03%, S：Less than 0.008, Ni： Less than 0.3%, Cr：15~20%, Al：Below N × 2~0.2%, N：Less than 0.01%, surplus by Fe and inevitably it is miscellaneous Texture into.Patent Document 2 discloses the heatproof ferrite series stainless steel that a kind of extrusion forming property is excellent, it contains Cr：11.0 ~20.0%, Si：Less than 1.5%, Mn：Less than 1.5%, C%+N%：0.02~0.06%, Zr：0.2~0.6%, and Zr%=10 (C%+N%) ± 0.15%, surplus is substantially made of Fe.In addition, Patent Document 3 discloses a kind of mouldability Excellent ferrite series stainless steel plate, it is characterised in that in terms of mass%, contain C：0.02~0.06%, Si：Less than 1.0%, Mn：Less than 1.0%, P：Less than 0.05%, S：Less than 0.01%, Al：Less than 0.005%, Ti：Less than 0.005%, Cr：11~ Less than 30%, Ni：Less than 0.7%, and satisfaction 0.06≤(C+N)≤0.12 and the side of 1≤N/C in terms of the relation with C content Formula contains N, and then 1.5 × 10- of satisfaction in terms of the relation with N content3≤(V×N)≤1.5×10-2Mode contain V, surplus It is made of Fe and inevitable impurity.In addition, Patent Document 4 discloses a kind of ferrite of excellent corrosion resistance is stainless Steel, it contains C in terms of weight %：Less than 0.02%, Si：Less than 1.0%, Mn：Less than 2.0%, Cr：11~35%, Ni： 0.5%th, N：Less than 0.03%, V：0.5~5.0%, surplus is made of iron and subsidiary impurity.
Patent document
Patent document 1：Japanese Unexamined Patent Application 52-24913 publications
Patent document 2：Japanese Unexamined Patent Application 54-112319 publications
Patent document 3：No. 3584881 publication of patent
Patent document 4：Japanese Unexamined Patent Application 59-193250 publications
The content of the invention
However, in technology described in patent document 1, due to premised on low N, so in the presence of steel process processed can not be avoided The problem of middle cost increases.
In addition, in technology described in patent document 2, due to adding substantial amounts of Zr, so it is mingled with object amount increase in steel, In the presence of the generation that can not avoid the problem that thus caused surface defect.
In addition, in technology described in patent document 3, as the index of mouldability, to improve elongation, r values and improve For the purpose of wrinkle resistance.However, for reducing intra-face anisotropy, (Δ r) is not accounted for completely, is existed in terms of molding processibility Problem.
In addition, in technology described in patent document 4, by adding V, so that corrosion resistance, particularly anticorrosion stress-resistant Disruptiveness significantly improves.However, not accounted for completely for molding processibility, there are problem in terms of molding processibility.
In this way, it is above-mentioned in the prior art, fail to solve the problems, such as follows：When carrying out stringent deep-draw deep processing, occur Wrinkle and cause the increase for grinding load, or easily causes non-uniform deformation.
The present invention is in view of the foregoing, it is therefore an objective to it is excellent to provide a kind of molding processibility for meeting deep drawability and wrinkle resistance Ferrite series stainless steel plate.
The inventors of the present invention have carried out various researchs to realize the above subject, it turns out that, by making V/B be more than 10 And the content of V, B is controlled the precipitates such as carbide in steel, nitride for optimum range, crystallization particle diameter can be made fine Change, realize the improvement of deep drawability, and suppress to wrinkle, the excellent ferrite series stainless steel plate of molding processibility is obtained, into one Step in the case that final annealing temperature changes in practical operation, can also suppress steel plate table by making V/B be more than 20 The acumenization (sensitization) in face, so as to complete the present invention.The purport of the present invention is as follows.
(1) a kind of ferrite series stainless steel plate, it is characterised in that in terms of quality %, contain C：0.010~0.070%, Si：Less than 1.00%, Mn：Less than 1.00%, P：Less than 0.040%, S：Less than 0.010%, Al：Less than 0.150%, Cr： 14.00~20.00%, Ni：Less than 1.00%, N：0.010~0.060%, and then, contain V：0.005~0.100%, B： 0.0001~0.0050% and meet V/B >=10, surplus is made of Fe and inevitable impurity.
(2) ferrite series stainless steel plate as described in (1), it is characterised in that Si：0.05~0.28%, Mn：0.05~ 0.92%.
(3) ferrite series stainless steel plate as described in (1) or (2), it is characterised in that meet that the ground of V/B >=20 contains V and B.
It should illustrate that in the present invention, the excellent ferrite series stainless steel plate of molding processibility refers to meet more than 30% Elongation (El), more than 1.3 r values, the ferrite series stainless steel plate of less than 0.3 Δ r.
In accordance with the invention it is possible to the molding processibility for being met deep drawability and wrinkle resistance it is excellent ferrite it is stainless Steel plate.
Brief description of the drawings
Fig. 1 is the figure of the relation for the engineering properties and V/B for representing cold rolled annealed plate, Fig. 1 (a) be represent elongation (El) with The figure of the relation of V/B, Fig. 1 (b) are the figures for the relation for representing r values and V/B, and Fig. 1 (c) is the figure for the relation for representing Δ r and V/B, Fig. 1 (d) is the figure for representing corrugation height and the relation of V/B.
Fig. 2 is the figure of the relation of the content of V, B for representing the acumenization characteristic for ensuring cold rolled annealed plate.
Embodiment
Hereinafter, the mode for implementing the present invention is described in detail.It should illustrate that the % of the amount of expression composition is not having Refer to quality % when having special instruction.
First, the component restriction reason of the ferrite series stainless steel plate of the present invention is illustrated.
C：0.010~0.070%
The austenite phase that C is dissolved in steel and contributes in hot rolling stabilizes, and is bonded with Cr and is used as Cr carbide Or the precipitation such as Cr carbonitrides are in crystal grain, grain boundary.But if C be less than 0.010%, cannot by V (C, N), VC、V4C3Etc carbonitride, carbide the micronized effect of crystal grain that brings of fine precipitation.In addition, the Ovshinsky in hot rolling Body phase fraction reduces, and therefore, in the cold-rolled steel sheet as sheet, corrugated generation becomes notable, molding processibility deterioration. On the other hand, if C excessively increases higher than 0.070%, Cr carbide contents or Cr carbonitride amounts, steel plate hardening, shaping adds Work reduces, and increases as de- Cr layers (the Cr depletion layer), thick precipitate, field trash for starting point of getting rusty Add.Therefore, it is 0.010%~0.070% to make C.More preferably 0.020~0.040%.
Si：Less than 1.00%
Si is useful element as the deacidification agent of steel.The effect, preferably more than 0.05% in order to obtain.But if More than 1.00%, then ductility reduces and molding processibility reduces.Therefore, Si is less than 1.00%.More preferably 0.05~ Less than 0.50%.If it is less than 0.28% to make Si, pickling becomes good, thus when needing pickling for 0.05%~ 0.28%.
Mn：Less than 1.00%
Mn is bonded with S present in steel and forms MnS, reduces corrosion resistance.Therefore, it is less than 1.00% to make Mn.It is more excellent Elect less than 0.80% as.On the other hand, due to beyond need low Mnization when refining cost increase, it is advantageous to 0.05% with On.It should illustrate that particularly from the viewpoint of the situation and refining cost for requiring high corrosion resistance, more preferably 0.05~ 0.60%.If it is less than 0.92% to make Mn, pickling becomes good, it is therefore desirable to during pickling for 0.05%~ 0.92%.
P：Less than 0.040%
P is the element being harmful to corrosion resistance, therefore is preferably reduced as far as possible.In addition, if more than 0.040%, then because Solution strengthening and cause processability to reduce.Therefore, P is less than 0.040%.More preferably less than 0.030%.
S：Less than 0.010%
S forms sulfide in steel.When containing Mn, is bonded with Mn and forms MnS.MnS is stretched because of hot rolling etc., in ferrite Crystal boundary etc. exists as precipitate (field trash).Such sulfide-based precipitate (field trash) reduces elongation, particularly Cracking when seriously affecting bending machining produces, therefore S is preferably reduced as far as possible, is allowed within 0.010%.It should say It is bright, it is preferably less than 0.005%.
Cr：14.00~20.00%
Cr is by steel solution strengthening, and helps to improve the element of corrosion resistance, is as first necessary to stainless steel plate Element.But if Cr is less than 14.00%, the corrosion resistance as stainless steel is insufficient.On the other hand, if Cr exceedes 20.00%, then toughness reduce, and steel overvulcanization and elongation is significantly reduced.Therefore, Cr is 14.00~20.00%. And then it is preferably 16.00~18.00% from the viewpoint of corrosion resistance and manufacturing.
Al：Less than 0.150%
Al is useful element as the deacidification agent of steel.The effect, preferably more than 0.001% in order to obtain.But excessively Addition can become the reason for causing surface defect because of the increase of Al systems field trash, so being less than 0.150%.More preferably Less than 0.100%.More preferably less than 0.010%.
Ni：Less than 1.00%
Ni has the effect for reducing crevice corrosion.The effect, preferably more than 0.05% in order to obtain.But it is expensive Element, and even if amount more than 1.00%, these effects also saturation, reduces hot-workability on the contrary.Therefore, Ni is Less than 1.00%.More preferably 0.05~0.40%.
N：0.010~0.060%
N contributes to the stabilisation of the austenite phase in hot rolling with being dissolved in the same manner as C in steel, and is bonded and makees with Cr For Cr nitride or Cr carbonitrides in crystal grain, grain boundary etc. separates out.In addition, it is bonded and shape with V important in the present invention Into nitride, carbonitride, make the crystal grain miniaturization of final products and help to improve r values.If N is less than 0.010%, heat Austenitic phase fraction in rolling reduces, therefore becomes notable as corrugated generation in the cold-rolled steel sheet of final products, and shaping adds Work deteriorates.On the other hand, excessively increase if amount nitrogenizes object amount or Cr carbonitrides amount more than 0.060%, Cr, steel Plate hardens, and elongation reduces.Therefore, N is 0.010~0.060%.More preferably 0.020~0.050%.
V：0.005~0.100%, B：0.0001~0.0050% and V/B >=10 more than
V and B is extremely important element in the present invention.V and N bonds together to form the nitride of VN, V (C, N) etc, carbon nitrogenizes Thing, has the effect for the coarse grains for suppressing hot-roll annealing plate.In addition, B has by being thickened in ferrite grain boundaries, delay is brilliant (grain boundary migration) is moved to aid in the effect that grain growth suppresses in boundary.Pass through the compound effect of these V and B Fruit, the crystal grain miniaturization of hot-roll annealing plate.As a result, the Preferential Nucleation site of { 111 } recrystal grain after cold rolled annealed The area increase of (preferential nucleation sites of the recrystallized grains) i.e. crystal boundary, { 111 } the recrystal grain increase in orientation, it is thus regarded that r values improve.Additionally, it is believed that the ratio of V amounts and B amounts crystallizes ferrite Particle diameter and ferrite grain boundaries area impact, and therefore, effect, the inventors of the present invention are improved in order to give play to r values to greatest extent The optimization of the content of V and B is studied.
Following steel is subjected to melting, by heating steel billet to after 1170 DEG C, carries out the hot rolling that final temperature is 830 DEG C, system Into hot rolled plate, the steel forms as component and contains C：0.04%th, Si：0.40%th, Mn：0.80%th, P：0.030%th, S： 0.004%th, Al：0.002%th, Cr：16.20%th, Ni：0.10%th, N：0.060%, V amounts, B amounts is changed and is with the addition of V and B. To these hot rolled plates 860 DEG C implement 8hr hot rolled plates annealing after, carry out pickling, then implement total reduction be 86% it is cold Roll, cold-reduced sheet is made.Then, to these cold-reduced sheets in an atmosphere to carry out pickling after the final annealing of 820 DEG C of implementation 30sec, The cold rolled annealed plate of thickness of slab 0.7mm is made.Elongation, r values, Δ r, corrugation height (ridging are obtained to gained cold rolled annealed plate height).The relation of the engineering properties (elongation, r values, Δ r, corrugation height) of V/B and cold rolled annealed plate is shown in Fig. 1. As shown in Figure 1, by meeting that V amounts are that more than 0.005%, B amounts are more than 0.0001% and V/B >=10, thus El, r value, Δ r, Corrugation height is met.
In the present invention, V is that 0.005~0.1%, B is 0.0001~0.0050% and V/B >=10.If exceed respectively 0.1%th, V and B is excessively added in 0.0050% ground, then not only suppresses the effect of miniaturization and the growth of the crystal grain in annealing, improves The effect saturation of molding processibility, on the contrary material curing, ductility reduce, molding processibility deterioration.It should illustrate that from ensuring Gao Yan From the aspect of property, more preferably V is that less than 0.005~0.03%, B is 0.0001~0.0020%.In addition, if V/B is than small In 10, then B is bonded with N and conduct nitride separates out, and thus B reduces in the effect that crystal boundary is thickened and suppresses grain growth, therefore Think that the raising of r values becomes inadequate.
In practical operation, final annealing temperature may not be constant, can not avoid heating time, reach the change of temperature.Such as Fruit anneals the ferrite series stainless steel plate of the stabilizing elements such as Ti, Nb for being not added with fixed C, N at high temperature, then sometimes Acumenization occurs in cooling procedure, crystal boundary is etched in pickling afterwards, so that surface quality deteriorates.Therefore, wide The item that acumenization does not occur in temperature range obtains becoming particularly important in terms of stabilizing quality in practical operation.
Therefore the inventors of the present invention have studied acumenization characteristic and the relation of V/B.Following steel is subjected to melting, by steel billet plus After hot to 1170 DEG C, the hot rolling that final temperature is 830 DEG C is carried out, hot rolled plate is made, the steel forms as component and contains C： 0.04%th, Si：0.40%th, Mn：0.80%th, P：0.030%th, S：0.004%th, Al：0.002%th, Cr：16.20%th, Ni： 0.10%th, N：0.060%, change V amounts, with the addition of V and B to B amounts.The hot rolled plate for implementing 8hr at 860 DEG C to these hot rolled plates moves back After fire, pickling is carried out, then implements the cold rolling that total reduction is 86%, cold-reduced sheet is made.Then, to these cold-reduced sheets in air In with 900 DEG C implementation 30sec final annealings after carry out pickling, the cold rolled annealed acid-cleaning plate of thickness of slab 0.7mm is made.Use scanning Formula electron microscope, to the crystal boundary in the region of 500 μm of 500 μ m of surface observation of the cold rolled annealed acid-cleaning plate of gained, investigation whether there is Grain-boundary attack (intergranular corrosion), evaluates surface quality.Acquired results are shown in Fig. 2.When not corroding Zero is evaluated as, be evaluated as when corroding ×.
As shown in Figure 2, V and B are added in a manner of meeting V/B >=20 by additive amount, even with 900 DEG C of annealing, Also the acumenization of crystal boundary can be suppressed.It is thought that due to C, N by making V fix in steel, reached even in final annealing temperature During to 900 DEG C of high temperature, the precipitation of the Cr carbonitrides at the grain boundary produced in the cooling after final annealing also can inhibit. On the other hand, if V/B is less than 20, B and is bonded with N and is used as nitride to separate out, thus the amount of precipitation of the carbonitride of V subtracts Few, as a result the amount of precipitation of Cr carbonitrides increases and the acumenization of crystal boundary is aggravated.It should illustrate that examined in terms of high ductility is ensured Consider, more preferably V is that 0.005~0.03%, B is 0.0001~0.0020%.
Surplus beyond above-mentioned chemical composition is Fe and inevitable impurity.It should illustrate that as inevitably miscellaneous Matter, such as permissible Nb：Less than 0.05%, Ti：Less than 0.05%, Co：Less than 0.5%, W：Less than 0.01%, Zr：0.01% Below, Ta：Less than 0.01%, Mg：Less than 0.0050%, Ca：0.0020% is such as the following.
Next, the manufacture method of the ferrite-group stainless steel of the present invention is illustrated.With generally well-known converter or The molten steel of the above-mentioned composition of electro-smelting, with vacuum outgas (RH), VOD (vacuum-oxygen decarbonizings：Vacuum Oxygen Decarburization), AOD (aods：Argon Oxygen Decarburization) etc. further refining after, it is excellent Choosing is cast using continuous casting process, and rolling blank (slab etc.) is made.Then, by rolling blank heating and hot rolling, thus it is made Hot rolled plate.The slab heating temperature of hot rolling is preferably 1050 DEG C~1250 DEG C of temperature range, in addition, going out from the viewpoint of manufacturing Hair, the final temperature of hot rolling is preferably 800~900 DEG C.For the purpose for improving the processability in subsequent handling, hot rolled plate can root Hot rolled plate annealing is carried out according to needs.Carry out hot rolled plate annealing when, preferably 700 DEG C~900 DEG C carry out 2 it is small when more than it is box Anneal (box annealing, batch annealing) or 900~1100 DEG C temperature range carry out the short time company Continuous annealing.It should illustrate that hot rolled plate can carry out the processing of deoxygenated skin and be directly prepared into product, cold rolling use in addition can also be made Blank.The cold rolling that cold rolling reduction ratio is more than 30% is implemented to the hot rolled plate of cold rolling blank, cold-reduced sheet is made.Cold rolling reduction ratio Preferably 50~95%.In addition, in order to further assign processability to cold-reduced sheet, can carry out more than 600 DEG C, preferably 700~ 900 DEG C of final annealing.Alternatively, it is also possible to which cold rolling-annealing is repeated 2 times.In addition, it is desirable to glossiness (glossiness) When can also implement skin-pass etc..The finish to gauge processing of cold-reduced sheet can carry out Japanese industrial Standard (JIS) 2D, 2B, BA specified in G4305 and various grindings.
Embodiment 1
Melting is carried out to the molten steel of the composition shown in table 1 using 2 refinings based on converter and VOD, utilizes continuously casting Slab is made in method.By these heating of plate blank to the hot rolling that final temperature is 830 DEG C after 1170 DEG C, is carried out, hot rolled plate is made.To this A little hot rolled plates carry out pickling after the 860 DEG C of hot rolled plate for implementing 8hr annealing, then implement the cold rolling that total reduction is 86%, system Into cold-reduced sheet.Then, oven gas is burnt with 1.3 air ratio, in the combustion atmosphere to steel No.1~18 and steel No.24~ 32 cold-reduced sheet is with the final annealing of 820 DEG C of implementation 30sec.Followed by pickling, is made the cold rolled annealed acid that thickness of slab is 0.7mm Board-washing.It should illustrate that pickling is the Na in 80 DEG C of temperature, 20 mass %2SO43 5A/dm of middle progress2After the electrolysis of × 10 seconds, 2 10A/dm are carried out in the nitric acid of 60 degree of 5 mass % of temperature2The electrolysis of × 5 seconds.Each sample can be removed completely by pickling Deoxidation envelope.
Table 1
Elongation, r values, Δ r are obtained to the cold rolled annealed acid-cleaning plate of gained, evaluates molding processibility.In addition, it is high to obtain corrugation Degree, evaluates wrinkle resistance.
In addition, make oven gas burn with 1.3 air ratio, to steel No.19~23 and 33~36 in the combustion atmosphere Cold-reduced sheet carries out pickling under conditions of same as described above, thickness of slab 0.7mm is made after 900 DEG C of final annealings for implementing 30sec Cold rolled annealed acid-cleaning plate.Each sample can remove oxide film thereon completely by pickling.The cold rolled annealed acid-cleaning plate of gained is carried out The evaluation of molding processibility and wrinkle resistance.Elongation, r values, Δ r, the assay method for the height that wrinkles are as follows.
(1) elongation
From all directions of cold rolled annealed acid-cleaning plate [rolling direction (L directions), rolling right angle orientation (C directions) and with rolling Direction direction at 45 ° (D directions)] collection JIS13 B test films.Implement tension test, measure using these tension test sheets The elongation of all directions.The average value of elongation is obtained by following formula using all directions elongation values.El is evaluated for more than 30% For qualification.
E1=(ElL+2 × ElD+ElC)/4
Here, ElL, ElD, ElC represent L directions, D directions, the elongation in C directions respectively.
(2) r values
From all directions of cold rolled annealed acid-cleaning plate [rolling direction (L directions), rolling right angle orientation (C directions) and with rolling Direction direction at 45 ° (D directions)] collection JIS13 B test films.According to the uniaxial tension that these test films are applied with 15% Width strain (width strain) and the r of the ratio measure all directions of thickness of slab strain (thickness strain) during prestrain It is worth (Lankford value (Lankford Value)), r values, Δ r is obtained by following formula.It is that more than 1.3, Δ r is less than 0.3 by r values It is evaluated as qualification.
R=(rL+2 × rD+rC)/4
Δ r=(rL-2 × rD+rC)/2
Here, rL, rD, rC represent the r values in L directions, D directions, C directions respectively.
(3) corrugation height
JIS5 tension test sheets are gathered from the rolling direction of cold rolled annealed acid-cleaning plate.Piece with #600 to these test films Face carries out smooth grinding, these test films are applied with prestrain (the prestrain of of 20% uniaxial tension Uniaxialstretching after), the relief height on the surface of roughness gauge determination test piece central portion is used.The relief height (height of the waviness) is the bumps produced because corrugation occurs.According to the height of fluctuating, by A：Less than 5 μm, B：More than 5 μm and it is less than 10 μm, C：More than 10 μm and it is less than 20 μm, D：This 4 Phase Evaluation wrinkle resistances more than 20 μm.Rise The height of volt is lower, then more beautiful after processing and forming.Using the A evaluations that the height of fluctuating is less than 5.0 μm as qualification.
Acquired results are shown in table 2.
Table 2
[table 2]
Any example be elongation be more than 30%, r values are more than 1.3, Δ r is less than 0.3, the height that rises and falls is Less than 5.0 μm of A evaluations, have good molding processibility and wrinkle resistance.On the other hand, in comparative example, be unsatisfactory for elongation, Any one of r values, Δ r, corrugation height.
Embodiment 2
To example No.5~11 and No.19~36 of the embodiment 1 with good mouldability and wrinkle resistance, evaluation acid Wash that ability is weaker than the acid wash of embodiment 1 and the nitrohydrochloric acid (mixed acid of nitric acid and hydrochloric acid that productivity is high：mixed acid of Nitric acid and hydrochloric acid) pickling in electrolysis (electrolytic method).To reality Manufactured steel No.5~11 and 19~36 thickness of slab 0.7mm cold-reduced sheets are applied in example 1 in weak reducing atmosphere (H2：5vol%, N2： 95vol%, dew point (dew point) -40 spend) under conditions of with 820 DEG C progress 30sec annealing, obtain cold rolled annealed plate.Will The cold rolled annealed plate is electrolysed in temperature 50 C, the solution being made of 10 mass % nitric acid and 1.0 mass % hydrochloric acid, visually Observation whether there is oxide film thereon residual, carries out the evaluation of pickling.
Will be by with 10A/dm2The situation that the electrolysis for carrying out 2 times in × 2 seconds just completely removes oxide film thereon is evaluated as ◎ (excellent), will be by with 10A/dm2The electrolysis for carrying out 2 times in × 2 seconds can not remove oxide film thereon completely and carry out 2 10A/dm2×4 The situation that oxide film thereon can be removed during the electrolysis of second completely is evaluated as zero (good), even if 2 10A/dm will be carried out2× 4 seconds The situation that electrolysis can not also remove oxide film thereon completely is evaluated as × (bad).◎ (excellent) and zero is (good) for qualification.
Show the result in table 3.
Table 3
[table 3]
Steel No.5~10,19~26 and 30~34 that Si is less than 0.28% and Mn is less than 0.92% not only processing and forming Property and wrinkle resistance are good, and pickling is especially excellent.General acid wash can be not only used, can also use large-duty nitre Electrolysis of hydrochloric acid method is produced.
Embodiment 3
Steel No.19~23 of embodiment 1 and 33~36 have been accounted for the scope of final annealing temperature in practical operation In change situation acumenization evaluation.
Acumenization evaluation method be by the cold-reduced sheet of manufactured thickness of slab 0.7mm in embodiment 1 900 DEG C anneal 30sec, press Condition same as Example 1 is in Na2SO4Nitric acid acidwashing is carried out after electrolysis.Using sweep electron microscope to cold rolled annealed acid The crystal boundary in the region of 500 μm of 500 μ m of surface observation of board-washing, investigation whether there is grain-boundary attack, evaluate surface quality.Crystal boundary does not produce It is evaluated as, without acumenization, sharpization being evaluated as when producing erosion during raw erosion.Show the result in table 4.
Table 4
[table 4]
Steel No. Acumenization is evaluated Remarks
19 There is sharpization Example
20 There is sharpization Example
21 Without acumenization Example
22 Without acumenization Example
23 Without acumenization Example
33 Without acumenization Example
34 Without acumenization Example
35 Without acumenization Example
36 Without acumenization Example
As shown in Table 4, V/B is more than 20 steel No.21~23 and 33~36 not only molding processibilities and crease-resistant Property it is good, and do not observe the generation of grain-boundary attack, resistance to acumenization characteristic is also good.
Industrial applicability
According to the present invention, by be optimized to packet into, particularly optimize V, B content, can manufacture meet deep drawability and Wrinkle resistance and the excellent ferrite series stainless steel plate of molding processibility, industrially play significant effect.In addition, by make V, The content of B is optimum range, can stably produce resistance to acumenization characteristic and improve, not only molding processibility is excellent, but also surface Quality also excellent ferrite series stainless steel plate.

Claims (3)

1. a kind of ferrite series stainless steel plate, it is characterised in that in terms of quality %, contain C：0.010~0.070%, Si： Less than 1.00%, Mn：Less than 1.00%, P：Less than 0.040%, S：Less than 0.010%, Al：Less than 0.150%, Cr：14.00 ~20.00%, Ni：Less than 1.00%, N：0.010~0.060%, and then, contain V：0.005~0.100%, B：0.0001~ 0.0050% and meet V/B >=10, surplus is made of Fe and inevitable impurity.
2. ferrite series stainless steel plate according to claim 1, it is characterised in that Si：0.05~0.28%, Mn：0.05 ~0.92%.
3. ferrite series stainless steel plate according to claim 1 or 2, it is characterised in that meet the ground of V/B >=20 contain V and B。
CN201711384153.0A 2012-09-24 2013-09-06 Ferritic stainless steel sheet having excellent formability Active CN107964632B (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2012-209100 2012-09-24
JP2012209100 2012-09-24
CN201380046801.5A CN104619874B (en) 2012-09-24 2013-09-06 The excellent ferrite series stainless steel plate of molding processibility

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
CN201380046801.5A Division CN104619874B (en) 2012-09-24 2013-09-06 The excellent ferrite series stainless steel plate of molding processibility

Publications (2)

Publication Number Publication Date
CN107964632A true CN107964632A (en) 2018-04-27
CN107964632B CN107964632B (en) 2021-01-22

Family

ID=50340884

Family Applications (2)

Application Number Title Priority Date Filing Date
CN201380046801.5A Active CN104619874B (en) 2012-09-24 2013-09-06 The excellent ferrite series stainless steel plate of molding processibility
CN201711384153.0A Active CN107964632B (en) 2012-09-24 2013-09-06 Ferritic stainless steel sheet having excellent formability

Family Applications Before (1)

Application Number Title Priority Date Filing Date
CN201380046801.5A Active CN104619874B (en) 2012-09-24 2013-09-06 The excellent ferrite series stainless steel plate of molding processibility

Country Status (6)

Country Link
JP (2) JP5614516B2 (en)
KR (1) KR101718757B1 (en)
CN (2) CN104619874B (en)
MY (1) MY160968A (en)
TW (1) TWI513831B (en)
WO (1) WO2014045542A1 (en)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107709591B (en) * 2015-07-02 2019-09-13 杰富意钢铁株式会社 Cold rolled stainless steel sheet raw material and its manufacturing method and cold-rolled steel sheet
SG11201909620RA (en) * 2017-04-19 2019-11-28 Nippon Steel Corp Cold rolled steel sheet for drawn can and method for manufacturing same
JP6432701B2 (en) 2017-04-25 2018-12-05 Ｊｆｅスチール株式会社 Ferritic stainless steel sheet and manufacturing method thereof
WO2018198834A1 (en) * 2017-04-25 2018-11-01 Ｊｆｅスチール株式会社 Ferritic stainless steel sheet, and production method therefor
WO2022085708A1 (en) * 2020-10-23 2022-04-28 日鉄ステンレス株式会社 Ferritic stainless steel, and method for manufacturing ferritic stainless steel

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001254154A (en) * 2000-03-13 2001-09-18 Kawasaki Steel Corp Ferritic stainless cold rolled steel sheet excellent in punchability and formability
JP2006299374A (en) * 2005-04-25 2006-11-02 Nippon Steel & Sumikin Stainless Steel Corp Ferritic stainless steel sheet superior in corrosion resistance and anti-ridging property, and manufacturing method therefor
JP2007270168A (en) * 2006-03-30 2007-10-18 Jfe Steel Kk Method for producing chromium-containing ferritic steel sheet
JP2011202231A (en) * 2010-03-25 2011-10-13 Nisshin Steel Co Ltd Method for producing hot rolled steel sheet having excellent pickling property and workability

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5949301B2 (en) 1975-08-21 1984-12-01 新日本製鐵株式会社 Ferritic stainless steel with excellent workability
JPS5924182B2 (en) 1978-02-23 1984-06-07 住友金属工業株式会社 Heat-resistant ferritic stainless steel with excellent press formability and its manufacturing method
JPS59193250A (en) 1983-04-15 1984-11-01 Sumitomo Metal Ind Ltd Ferrite type stainless steel excellent in corrosion resistance
DE3672280D1 (en) * 1985-02-19 1990-08-02 Kawasaki Steel Co VERY SOFT STAINLESS STEEL.
CN1043532A (en) * 1988-12-14 1990-07-04 抚顺钢厂 High-purity ferrite stainless steel
JP3132728B2 (en) * 1989-09-07 2001-02-05 日新製鋼株式会社 Ferritic stainless steel with excellent formability
JP3210255B2 (en) * 1995-10-25 2001-09-17 川崎製鉄株式会社 Ferritic stainless steel with excellent corrosion resistance and manufacturability
JPH10330891A (en) * 1997-05-27 1998-12-15 Nippon Steel Corp Ferritic stainless steel sheet excellent in cold rollability and its production
KR100484037B1 (en) * 1999-03-30 2005-04-18 제이에프이 스틸 가부시키가이샤 Ferritic stainless steel sheet having excellent formability
JP2001089814A (en) * 1999-09-22 2001-04-03 Kawasaki Steel Corp Method of manufacturing ferritic stainless steel sheet excellent in ductility, workability and ridging resistance
JP2001107149A (en) * 1999-09-30 2001-04-17 Kawasaki Steel Corp Method for producing ferritic stainless steel sheet excellent in ductility, workability and ridging resistance
WO2002018666A1 (en) * 2000-08-31 2002-03-07 Kawasaki Steel Corporation Low carbon martensitic stainless steel and method for production thereof
EP1514949B1 (en) * 2002-06-17 2015-05-27 JFE Steel Corporation FERRITIC STAINLESS STEEL PLATE WITH Ti AND METHOD FOR PRODUCTION THEREOF
KR100957664B1 (en) * 2004-01-29 2010-05-12 제이에프이 스틸 가부시키가이샤 Austenitic-ferritic stainless steel sheet

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001254154A (en) * 2000-03-13 2001-09-18 Kawasaki Steel Corp Ferritic stainless cold rolled steel sheet excellent in punchability and formability
JP2006299374A (en) * 2005-04-25 2006-11-02 Nippon Steel & Sumikin Stainless Steel Corp Ferritic stainless steel sheet superior in corrosion resistance and anti-ridging property, and manufacturing method therefor
JP2007270168A (en) * 2006-03-30 2007-10-18 Jfe Steel Kk Method for producing chromium-containing ferritic steel sheet
JP2011202231A (en) * 2010-03-25 2011-10-13 Nisshin Steel Co Ltd Method for producing hot rolled steel sheet having excellent pickling property and workability

Also Published As

Publication number Publication date
TWI513831B (en) 2015-12-21
JP5614516B2 (en) 2014-10-29
WO2014045542A1 (en) 2014-03-27
JPWO2014045542A1 (en) 2016-08-18
KR20150038601A (en) 2015-04-08
TW201420780A (en) 2014-06-01
MY160968A (en) 2017-03-31
JP5850090B2 (en) 2016-02-03
CN104619874B (en) 2018-07-10
CN107964632B (en) 2021-01-22
CN104619874A (en) 2015-05-13
JP2014205917A (en) 2014-10-30
KR101718757B1 (en) 2017-03-22

Similar Documents

Publication Publication Date Title
EP2554699B1 (en) Steel sheet with high tensile strength and superior ductility and method for producing same
JP5206244B2 (en) Cold rolled steel sheet
US6458221B1 (en) Ferritic stainless steel plate
JP5549414B2 (en) Cold-rolled thin steel sheet having excellent shape freezing property and manufacturing method thereof
KR100500791B1 (en) FERRITIC Cr-CONTAINING STEEL SHEET HAVING EXCELLENT DUCTILITY, FORMABILITY, AND ANTI-RIDGING PROPERTIES, AND METHOD OF PRODUCING THE SAME
KR20120008033A (en) Cold-rolled steel sheet having excellent slow-aging property and high curability in baking, and method for producing same
CN104685086B (en) Ferrite series stainless steel plate
CN104619874B (en) The excellent ferrite series stainless steel plate of molding processibility
WO2017168957A1 (en) Thin steel sheet, plated steel sheet, method for producing hot-rolled steel sheet, method for producing cold-rolled full hard steel sheet, method for producing thin steel sheet, and method for producing plated steel sheet
KR20160105869A (en) Ferritic stainless steel and method for producing same
CN102639740B (en) Steel sheet for cans and method for producing same
JP4065579B2 (en) Ferritic stainless steel sheet with small in-plane anisotropy and excellent ridging resistance and method for producing the same
CN105378134A (en) Steel sheet for can, and method for manufacturing same
KR101264537B1 (en) Method for manufacturing steel plate for can-making
JP2010133028A (en) Method for manufacturing high-strength low-specific gravity steel sheet excellent in ductility
JP3932020B2 (en) Ferritic stainless steel with excellent deep drawability and small in-plane anisotropy and method for producing the same
JPH08253818A (en) Production of ferritic stainless steel strip reduced in inplane anisotropy and excellent in balance between strength and elongation
JP5045050B2 (en) Ferritic stainless hot rolled steel sheet for cold rolling and method for producing the same
JP2009102673A (en) High-tension cold-rolled steel sheet, high tension galvanized steel sheet, and producing method therefor
JP2007162138A (en) Steel sheet for nitriding treatment and its production method
WO2021039499A1 (en) Low-strength steel sheet for hot stamping, hot-stamped component, and method for manufacturing hot-stamped component
KR20040110644A (en) Ferritic stainless steel having an excellent elongation percentage and method thereof
KR20220081556A (en) Ferritic stainless steel with improved ridging resistance and its manufacturing method
JPH11229038A (en) Production of ferritic stainless steel sheet excellent in surface quality, ridging resistance and formability

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant