CN102933732B - The excellent structure stainless steel plate of corrosion resistance at welded part and its manufacture method - Google Patents
The excellent structure stainless steel plate of corrosion resistance at welded part and its manufacture method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B9/00—Measures for carrying out rolling operations under special conditions, e.g. in vacuum or inert atmosphere to prevent oxidation of work; Special measures for removing fumes from rolling mills
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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Abstract
The present invention provide it is a kind of can at a low price and expeditiously produce, the structure stainless steel plate of the excellent corrosion resistance of weld part and its manufacture method.Specifically, contained in terms of quality %：C：0.01~0.03%, N：0.01~0.03%, Si：0.01~0.40%, Mn：1.5~2.5%, P：Less than 0.04%, S：Less than 0.02%, Al：0.05~0.15%, Cr：10~13%, Ni：0.5~1.0%, Ti：4×（C+N）Above, less than 0.3%, also, be defined to V：Less than 0.05%, Ca：Less than 0.0030%, O：Less than 0.0080%, moreover, with Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 ×（C+N）The F values of expression meet less than 11, with Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 ×（Ni+Cu）- 40 ×（C+N）The FFV values that+20 × V is represented meet less than 9.0, and remainder is made up of Fe and inevitable impurity.
Description
Technical field
The present invention relates to be adapted as transporting such as coal（coal）, iron ore（ironore）Lorry（Railway freight-car（railwaywagon））Vehicle body purposes material, weld part corrosion resistance（corrosionresistance）Excellent structure stainless steel plate（structuralstainlesssteelsheet）And its manufacture method.
Background technology
Transport coal, the lorry of iron ore（Railway freight-car）Vehicle body purposes material more use stainless steel.Because the coal being pooled out out largely contains sulphur composition（sulfurcontent）, therefore the material requirements corrosion resistance to sulfuric acid of the vehicle body of railway freight-car（sulfatecorrosionresistance）, particularly weld part resistance to intergranular corrosion（intergranularcorrosionresistance）.
As the stainless steel for having corrosion resistance and weldability concurrently, for example Patent Document 1 discloses the ferrite-group stainless steel containing Ti of the tenacity excellent of weld part.But, in the technology of patent document 1, so that the tissue of weld part turns into ferritic phase（ferritephase）Ground carries out composition design, therefore there is the toughness of weld part（toughness）, corrosion resistance and this insufficient problem.
In this regard, disclosing following technology in patent document 2,3：By controlling the phase fraction under high temperature, so as to generate appropriate martensitic phase in weld part（martensiticphase）, improve the processability of weld part（workability）, corrosion resistance.In addition, Patent Document 4 discloses be adapted in use to carbon dioxide（carbondioxidegas）Welding stainless steel.In addition, the people in the present inventor proposes a kind of structure stainless steel plate, wherein, first by can correctly predicted weld part tissue parameter（parameter）, composition is constituted and rationalized, so as to improve the corrosion resistance of weld part（Patent document 5）.
Patent document 1:Japanese Unexamined Patent Publication 3-249150 publications
Patent document 2:Japanese Unexamined Patent Publication 2002-167653 publications
Patent document 3:Japanese Unexamined Patent Publication 2009-13431 publications
Patent document 4:Japanese Unexamined Patent Publication 2002-30391 publications
Patent document 5:Japanese Unexamined Patent Publication 2009-280850 publications
The content of the invention
However, in technology disclosed in these patent documents 2 ~ 5, the research for most suitable composition range may not be abundant.Especially these almost do not account for manufacturing（manufacturability）, the steel billet stage（slabstage）Crackle generation and be referred to as scabbing（scab）Surface defect（surfacedefect）Generation it is notable, it is difficult to avoid because of yield rate（yieldratio）Cost increase caused by declining（costrise）.
The present invention is completed in view of the foregoing, and its object is to provide a kind of structure stainless steel plate of the excellent corrosion resistance of can at a low price and expeditiously produce, weld part.
A people in the present inventor is had found chemical composition, particularly Mn, Ti content and the balance of each composition for the result that the above-mentioned problem of solution has made intensive studies（balance）Proper range is adjusted to, then can suppress the intercrystalline corrosion because of caused by Cr missings near grain boundary（intergranularcorrosion）, and can be by welding heat affected zone（weldedheataffectedzone）Be formed as with martensite（martensite）For the tissue of main body, so as to propose the parameter shown in patent document 5（F values）.And then, the present inventor etc. are based on above opinion, particularly the result that manufacturing continues to study in detail is found in right amount containing on the basis of Al, V, Ca, O are reduced to below prescribed limit, and appropriate scope will be set as the FFV values for representing the good and bad new parameter of manufacturing, thus, it is possible to be remarkably decreased crackle of steel billet（slabcrack）Scabbed with caused by field trash（Surface defect）, so as to complete the present invention.
That is, the present invention provides a kind of corrosion resistance at welded part excellent structure stainless steel plate, it is characterised in that in terms of quality %, contain：C：0.01~0.03%、N：0.01~0.03%、Si：0.10~0.40%、Mn：1.5~2.5%、P：Less than 0.04%, S：Less than 0.02%, Al：0.05~0.15%、Cr：10~13%、Ni：0.5~1.0%、Ti：4×（C+N）~0.3%（Wherein, C, N represent the content of these elements（Quality %））, also, it is defined to V：Less than 0.05%, Ca：Less than 0.0030%, O：Less than 0.0080%, moreover, the F values and FFV values that are represented with following formula meet F value≤11, FFV value≤9.0, remainder is made up of the inevitable impurity of Fe and F.
F values=Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 ×（C+N）
FFV values=Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 ×（Ni+Cu）-40×（C+N）+ 20 × V
Wherein, in these formulas, each element symbol is the content of these elements（Quality %）.
In addition, the present invention provides a kind of corrosion resistance at welded part excellent structure stainless steel plate, it is characterised in that on the basis of mentioned component, in terms of quality %, also contain Cu：Less than 1.0%.
In addition, the present invention provides a kind of corrosion resistance at welded part excellent structure stainless steel plate, it is characterised in that on the basis of mentioned component, in terms of quality %, also contain Mo：Less than 1.0%.
In addition, the present invention provides a kind of manufacture method of structure stainless steel plate, characterized in that, by after the temperature of heating steel billet to 1100 ~ 1300 DEG C, hot rolling is carried out in the temperature province more than 1000 DEG C, or, after being hot-rolled as described above, hot rolled plate do not annealed or implements pickling after being annealed at a temperature of 600 ~ 1000 DEG C, wherein, is included in the hot rolling at least carry out hot roughing of the reduction ratio of more than 1 time for more than 30% rolling
The steel billet has consisting of, i.e. in terms of quality %, contain：C：0.01~0.03%、N：0.01~0.03%、Si：0.10~0.40%、Mn：1.5~2.5%、P：Less than 0.04%, S：Less than 0.02%, Al：0.05~0.15%、Cr：10~13%、Ni：0.5~1.0%、Ti：4×（C+N）~0.3%（Wherein, C, N represent the content of these elements（Quality %））, and it is defined to V：Less than 0.05%, Ca：Less than 0.0030%, O：Less than 0.0080%, moreover, the F values and FFV values that are represented with following formula meet F value≤11, FFV value≤9.0, remainder is made up of Fe and inevitable impurity.
F values=Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 ×（C+N）
FFV values=Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 ×（Ni+Cu）-40×（C+N）+ 20 × V
Wherein, in these formulas, each element symbol is the content of these elements（Quality %）.
In addition, the present invention provides a kind of manufacture method of the excellent structure stainless steel plate of corrosion resistance at welded part, it is characterised in that on the basis of mentioned component, in terms of quality %, also contain Cu：Less than 1.0%.
In addition, the present invention provides a kind of manufacture method of the excellent structure stainless steel plate of corrosion resistance at welded part, it is characterised in that on the basis of mentioned component, in terms of quality %, also contain Mo：Less than 1.0%.
Can low price and expeditiously produce, lorry being adapted as transporting such as coal, iron ore in accordance with the invention it is possible to obtain（Railway freight-car）Vehicle body purposes material, weld part excellent corrosion resistance structure stainless steel plate.
Brief description of the drawings
Fig. 1 is the coordinate diagram for the relation for representing FFV values and surface defect incidence.
Fig. 2 is the optical microscope photograph for representing to can confirm that the observation example of the situation of the corrosion of dell shape in the test film section welding heat affected zone after sulfuric acid-copper sulphate corrosion test.
Embodiment
Hereinafter, the present invention is described in detail.
First, the composition composition of the present invention is illustrated.In illustrating below, % represents quality %.
·C：0.01~0.03%
·N：0.01~0.03%
In order to obtain as the intensity required for structure stainless steel plate, C and N are required to containing more than 0.01%.On the other hand, if C, N content are more than 0.03%, Cr carbide or Cr carboritrides become easy precipitation, the corrosion resistance of corrosion resistance, particularly welding heat affected zone declines.In addition, welding heat affected zone solidifies, toughness also declines.Therefore, make C and N content be 0.01 ~ 0.03% scope.More preferably C is the scope that 0.015 ~ 0.025%, N is 0.012 ~ 0.02%.
·Si：0.10~0.40%
Si is the element that can be used as deoxidier, in order to obtain the effect, it is necessary to contain more than 0.10%.On the other hand, if its content is more than 0.40%, decline the toughness of hot rolled steel plate.Therefore, the scope that Si contents are 0.10 ~ 0.40% is made.Preferably lower limit is 0.20%, and the upper limit is 0.30%.
·Mn：1.5~2.5%
Mn is as deoxidier, and it, as the useful element of the intensified element for ensuring the intensity required for structure stainless steel plate, is also the austenite stabilizer element under high temperature to be.In addition, being element important in terms of the microstructure of welding heat affected zone is controlled as the martensitic structure with desired volume fraction in the present invention.In order to play such effect, its content is necessary for more than 1.5%.On the other hand, containing more than 2.5%, then its effect not only can saturation, content becomes excessive and declines toughness, also declines the desquamation in manufacturing process, surface texture is negatively affected, and cost of alloy also increases.Therefore, the scope that the content for making Mn is 1.5 ~ 2.5%.More preferably 1.8 ~ 2.5% scope.More preferably 1.85 ~ 2.0% scope.
·P：Less than 0.04%
From the viewpoint of hot-workability, preferably P is more few better, and the admissible higher limit of its content is set into 0.04%.More preferably less than 0.035%.
·S：Less than 0.02%
From the viewpoint of hot-workability and corrosion resistance, preferably S is more few better, and the admissible higher limit of its content is set into 0.02%.Preferably less than 0.005%.
·Al：0.05~0.15%
Contain generally for deoxidation in Al, but the present invention, it is found that Al can be to manufacturing, the suppression particularly to the crackle generation in the steel billet stage is effectively worked, and is contained in right amount to play such function.It is described as be described hereinafter to also need to reduce V, Ca, O on the basis of containing Al in order to suppress the generation of crackle of steel billet, and need to optimize FFV values.It is still not clear by the mechanism that can improve crackle of steel billet containing Al, but speculates it is because of caused by the rationalization of phase fraction and the effect of control inclusion morphology.In order to obtain such effect, it is necessary to containing more than 0.05% Al.On the other hand, if its content is more than 0.15%, the reason for large-scale Al systems field trash is so as to as surface defect is generated.Therefore, the scope that the content for making Al is 0.05 ~ 0.15%.More preferably 0.080 ~ 0.150% scope.More preferably 0.085 ~ 0.120% scope.
·Cr：10~13%
Cr is to form passivation envelope, it is ensured that corrosion resistance, is especially to ensure that necessary element in terms of the corrosion resistance of welding heat affected zone, in order to obtain the effect, it is necessary to contain more than 10%.On the other hand, if being more than 13% containing Cr, not only cost increase, is also difficult to ensure enough austenite phases at high temperature, it is difficult to the martensitic structure of point rate required for the welding heat affected zone after being welded in weld part.As a result, causing the decline of the resistance to intergranular corrosion of welding heat affected zone.Therefore, the scope that Cr contents are 10 ~ 13% is made.Preferably 10.5 ~ 12.5%.
·Ni：0.5~1.0%
For the purpose of ensuring that intensity and the purpose of toughness, contain more than 0.5% Ni.On the other hand, Ni is the element of high price, and from the viewpoint of economy, its upper limit is set into 1.0%.It should illustrate, Ni is the austenite stabilizer element under high temperature in the same manner as Mn, it is useful in terms of the microstructure of welding heat affected zone is controlled into the martensitic structure with desired volume fraction, but in the present invention, its effect can fully be obtained by adding Mn, thus Ni content be preferably 0.5 ~ 1.0% scope.More preferably 0.60 ~ 1.0% scope.More preferably 0.60 ~ 0.90% scope.
·Ti：4×（C+N）~0.3%
Ti is is used to obtain the important element of excellent corrosion resistance at welded part in the present invention, especially for element necessary to the resistance to intergranular corrosion for improving welding heat affected zone.Ti using C, N in steel as Ti carbide, nitride or carboritride（After, carbide, nitride, this 3 kinds of carboritride are generally called, carboritride etc. is designated as）Separate out and fix, the effect of the generation with the carboritride for suppressing Cr etc..In the present invention, the welding heat affected zone of steel plate has the tissue being made up of ferrite and martensite, and from this angle of corrosion resistance, the ferritic phase part in cooling with the precipitation of carboritride etc., the lower general who has surrendered of corrosion resistance turns into problem.In the steel plate of the present invention, separated out by solving Cr carboritride etc. on the welding heat affected zone in welding containing Ti, Cr missings thus occur near grain boundary, particularly the problem of ferritic phase part resistance to intergranular corrosion declines.In order to play such effect, it is necessary to Ti content is set into 4 ×（C+N）More than（Wherein, C, N represent the content of these elements（Quality %））.On the other hand, a large amount of Ti carboritride etc. is also separated out in steel, causes degraded toughness largely containing then its effect not only saturation more than 0.3%.Therefore, Ti content be set to 4 ×（C+N）~0.3%.More preferably 0.180 ~ 0.230% scope, effectively so that Ti content simultaneously meet 4 ×（C+N）Mode above reduces C, N.
In the present invention, for productivity ratio（Qualification rate）, manufacturing, especially for suppressing the steel billet stage crackle produced and scabbing of producing by field trash（Surface defect）, it is important that reduce V, Ca, O by following.
·V：Less than 0.05%
V mostly as Cr raw materials etc. impurity and by containing, be sometimes non-original meaning contain, but especially for suppress the steel billet stage crackle generation, it is necessary to its content of considered critical.From the above point of view, it is necessary to which V content is set into less than 0.05%.It is preferred that scope be less than 0.03%, further preferred range be less than 0.03%.By making content be less than 0.01%, more preferable crackle inhibition can be obtained, but due to needing the screening of progress raw material, therefore it is economically disadvantageous.
·Ca：Less than 0.0030%
Ca is the field trash for generating low melting point, can particularly be turned into because of the reason for surface defect caused by field trash.Therefore, its content of considered critical is needed in the present invention, its upper limit is set to 0.0030%.Ca contents are more low more preferred, and preferably 0.0010%, more preferably less than 0.0002%, but need to carry out raw material screening, therefore it is economically disadvantageous.
·O：Less than 0.0080%
In order to suppress the generation of oxide system field trash, it is ensured that its upper limit is set to 0.0080%, it is necessary to reduce O content by high production rate.Preferably less than 0.0060%.
Moreover, in the present invention, being set to appropriate scope by making F values as shown below, FFV values, greatly improving corrosion resistance, productivity ratio.
F value≤11
F values with Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 ×（C+N）Represent（Wherein, each element symbol is the content of these elements（Quality %））, it is the microstructure of welding heat affected zone when judging welding（microstructure）Parameter, be more specifically the volume fraction for judging martensitic structure（The remaining rate of ferritic structure）Parameter.In the position being exposed to as welding heat affected zone under high temperature, one part metamorphosis is austenite（austenite）（Or it is delta ferrite that a part is further abnormal（deltaferrite））, it is martensite that this is abnormal in cooling procedure.Its ratio is by ferrite stabilizer（Ferrite generating elements（ferriteformationelements））With austenite stabilizer element（Austenite forming element（austeniteformationelements））Amount balance influence.It is positive element to represent the coefficient in the formula of above-mentioned F values（Cr、Si、Ti）For ferrite stabilizer, coefficient is negative element（Ni, Mn, C, N）For austenite stabilizer element.That is, the easier residual of the bigger ferritic structure of F values（The volume fraction of ferritic structure is big, i.e. the volume fraction of martensitic structure is small）, smaller ferritic structure is more difficult to remain（The volume fraction of ferritic structure is small, i.e. the volume fraction of martensitic structure is big）.
In patent document 5, investigate F values and the relation of the volume fraction of the martensitic structure of welding heat affected zone, the corrosion resistance near welding heat affected zone is further evaluated by sulfuric acid-copper sulphate corrosion test, so as to realize the optimization of composition, and in the present invention also in the same manner as above-mentioned patent document 5, for the raising of the corrosion resistance of realizing welding heat affected zone, above-mentioned F values are set to less than 11（Martensitic volume rate：More than 40%）.It is preferred that F values：Less than 10.5（Martensitic volume rate more than 60%）, more preferably less than 10.It should illustrate, from the viewpoint of the corrosion resistance of weld part, the lower limit of F values is preferably set to more than 5.0.Further preferred range is more than 6.0.
FFV value≤9.0
FFV values with Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 ×（Ni+Cu）-40×（C+N）+ 20 × V is represented（Wherein, each element symbol is the content of these elements（Quality %））, it is as the new derived value of the index for representing manufacturing in the present invention.The FFV values are to consider the value balanced each other in hot rolling, therefore above-mentioned composition adjustment is carried out, particularly carry out on the basis of the containing of Al, the restriction of V, Ca, O upper limit, reduce the value, so as to substantially reduce the generation of the surface defect because of caused by the crackle and field trash in steel billet stage.The present invention is noteworthy characterized by the optimization for the new parameter that the Al amounts not considered when being designed by realizing F values are accounted for, so as to successfully significantly inhibit the decline of the yield rate caused by the generation of surface defect.Although FFV values not yet completely clearly, by the way that FFV values are set into less than 9.0, so as to significantly improve manufacturing, therefore are set to less than 9.0 by the mechanism that manufacturing caused by the optimization of FFV values improves.Preferably less than 8.5.It should illustrate, in order to reduce FFV values, effectively reduce Cr amounts, increase C, N amount, so then there is a possibility that corrosion resistance declines.It is therefore preferable that the lower limit of FFV values is set into more than 5.0.Further preferred range is more than 6.0.
In the steel plate of the present invention used with the state of hot rolled plate or hot-roll annealing plate, in order to reduce surface defect, it is important that the crackle and field trash in control steel billet stage.The generation of surface defect not only makes yield rate decline to a great extent, crackle, the apparent variation for this part of scabbing, and will also become the starting point that rust is produced, therefore as object part must be cut off during product export.Should illustrate, Mo, V, Cu are contained in the formula of above-mentioned FFV values, but also have these situation is not contained in steel, when not containing these, by it is therein do not contain calculate FFV values into being divided into 0%.
Fig. 1 represents the relation of FFV values and surface defect incidence.For the incidence of defect, it is known that less than 9.0 appropriate scope is set to by the FFV values for obtaining the length computation of the part occurred relative to coil of strip total length by defect, so as to significantly inhibit the generation of surface defect.
, can be as needed in addition to mentioned component in the present invention, contain Cu in following scope.
·Cu：Less than 1.0%
Cu is the element for improving corrosion resistance, particularly makes crevice corrosion（crevicecorrosion）The element of reduction.Therefore, it can be added in the case where requiring highly corrosion resistant.But, it is more than 1.0%, hot-workability if contained（hotworkability）Decline, and balancing each other under high temperature is broken, and is difficult to obtain desired tissue in welding heat affected zone.Therefore, in the case of containing Cu, its upper limit is set to 1.0%.Corrosion resistance effect is improved in order to give full play to, effectively containing more than 0.3%.Preferred scope is 0.3 ~ 0.5%.
·Mo：Less than 1.0%
Mo is the element for improving corrosion resistance, can particularly be added in the case where requiring highly corrosion resistant.But, if containing being more than 1.0%, cold-workability declines, and causes the surface roughening under hot rolling, and surface quality extremely declines.Therefore, in the case of containing Mo, its upper limit is set to 1.0%.In order to give full play to corrosion resistance, effectively containing more than 0.03%.More preferably scope is 0.1 ~ 1.0%.
In the present invention, except improving corrosion resistance as described above by Cu, Mo containing less than 1.0%, other elements can also be contained according to conventional knowledge, such as improving ductility by the B containing less than 0.005%, and consider the no less important that balances each other under high temperature in this case.Should illustrate, Nb be strong stability element, combined with C, N and significantly destroy and balance each other, thus in the present invention without.It should illustrate, the remainder beyond element defined above is Fe and inevitable impurity.
For the steel plate of the present invention, in order to realize the corrosion resistance for improving welding heat affected zone, by the way that above-mentioned F values are set into less than 11, so that the martensitic volume rate of welding heat affected zone is more than 40%.F values are further preferably set to less than 10.5, thus making the martensitic volume rate of welding heat affected zone turns into more than 60%.More preferably less than 10, martensitic volume rate now is more than 80%.In addition, in the steel plate of the present invention, mother metal portion in terms of volume fraction more than 50% is ferritic structure., particularly in the state of the former state of hot rolling, there is martensitic phase and remnants γ phases, a part of tissue containing carboritride etc. in the tissue of remainder.It is particularly as hereinafter described be set to appropriate compositing range and implement the hot-roll annealing plate after hot rolled plate annealing under appropriate annealing conditions tissue when almost 100% there is ferritic phase tissue in terms of volume fraction, processability is very excellent.
Next, the manufacture method to the stainless steel plate of the present invention is illustrated.
The manufacture method of stainless steel plate of the present invention is carried out according to conventional methods, is not particularly limited, but as can high efficient production method, recommendation following methods：The steel for being smelted into mentioned component composition is made up after steel billet of continuously casting etc., coils of hot-rolled steel is made, after being annealed as needed to it, de-scaling is carried out（descaling）（Shot-peening（shotblasting）, pickling（pickling）Deng）, the stainless steel plate of the present invention is made.
Hereinafter, it is described in detail.
First, converter is utilized（steelconverter）Or electric furnace（electricfurnace）The molten steel constituted etc. usually used known smelting furnace to the composition for being adjusted to the present invention carries out melting, then, utilizes vacuum outgas（RH methods）、VOD（VacuumOxygenDecarburization）Method, AOD（ArgonOxygenDecarburization）Method of refining known to method etc. is refined, then, utilizes continuous casting process（continuouscasting）Or steel billet is made in ingot casting-cogging method（Steel material）.From the viewpoint of productivity ratio and quality, the preferred continuously casting of casting.In addition, in order to ensure the reduction ratio described later using hot roughing, steel billet thickness preferably is set into more than 100mm.Preferred scope is more than 200mm.
Then, hot rolling after the temperature of heating steel billet to 1100 ~ 1300 DEG C, will be carried out and hot rolled steel plate is made.In order to prevent the surface roughening of hot rolled plate（surfaceroughnessresistance）With wrinkle properties of the raising after cold rolled annealed（anti-ridgingpropertyorridgingproperty）, billet heating temperature is more high more preferred, but more than 1300 DEG C, then steel billet is sagging（slabsag）Significantly, and coarse grains so that hot rolled plate toughness decline.On the other hand, if the heating-up temperature less than 1100 DEG C, then the load in hot rolling is increased, and the surface roughening in hot rolling becomes notable, and the recrystallization in hot rolling（recrystallization）Become insufficient, the toughness of hot rolled plate can still decline.
It is preferred that the process of hot roughing is in the temperature province more than 1000 DEG C, reduction ratio is at least carried out more than 1 time for more than 30% rolling.By this suppress it is lower rolled so that the crystalline structure granular of steel plate, improve toughness.After hot roughing, according to well-established law（The condition of common hot finishing）, carry out hot finishing.
2.0 ~ the 8.0mm of thickness of slab manufactured by hot rolling or so hot rolled plate can be directly used as structural material, or, it is not annealed and carry out after pickling be used as structural material.For hot rolled plate, implement pickling after being annealed at a temperature of 600 ~ 1000 DEG C to hot rolled plate.The annealing temperature of hot rolled plate then can still remain martensitic phase that may be present under the former state state of hot rolling, remnants γ phases, ferritic structure is in terms of volume fraction by as less than 50%, it is impossible to obtain sufficient processability sometimes if less than 600 DEG C.On the other hand, if greater than 1000 DEG C, then significantly, toughness declines the coarsening of crystal grain.The annealing of hot rolled plate preferably passes through so-called pot annealing（boxannealing）Kept for more than 1 hour at a temperature of defined 600 ~ 1000 DEG C.In addition, if annealing temperature is too high, then reaches sometimes and produce the abnormal temperature of γ, thus it is not preferred.Appropriate scope is adjusted to accordingly, it would be desirable to will constitute and selection is to the appropriate temperature range that should constitute.In the compositing range of steel of the present invention, in the case of the annealing temperature for being substantially set to 600 ~ 900 DEG C, in terms of volume fraction, almost 100% turns into ferritic phase, thus the preferably temperature range.
In the welding of the stainless steel plate of the present invention, TIG weld, MIG are welded as the arc welding represented（arcwelding）, seam weld（seamwelding）, spot welding（spotwelding）Etc. resistance welding, laser welding（laserwelding）It can be used etc. common welding method.
Embodiment
The thick steel billets of 200mm are made in the stainless steel with the composition composition shown in table 1 using converter-VOD- continuous casting processes.After the temperature of these heating steel billets to 1180 DEG C, the hot rolled plate of thickness of slab 5.0mm coiled material shape is made up of hot rolling.Hot rolling end temp is 900 DEG C, and the coiling temperature after hot rolling is 700 DEG C.To obtained hot rolled steel plate after 690 DEG C of annealing for carrying out 10 hours, shot-peening and pickling are carried out, except scaling（Oxide-film）.
From these eliminate the steel plate after squama in cut out plane plate specimen（flatplatesample）, the T-shaped test body being made up of lower plate and vertical panel is assembled, the welded corner joint of one layer of both sides is carried out（bothsideonepassfilletwelding）（Gas metal arc welding（gasmetalarcwelding）, protective gas（shieldinggas）：98 capacity %Ar-2 capacity %O2, flow：20 liters/min）, three welded corner joint test films are made.Solder bar uses Kobe Steel Ltd company system MGS-309LS, and heat input is 0.4 ~ 0.8kJ/mm scope.
Corrosion test piece is taken from the fillet welding socket part of these welded corner joint test films, sulfuric acid-copper sulphate corrosion test is carried out（ModifiedStrausstest, testing liquid based on ASTMA262practiceE and ASTMA763practiceZ are Cu/6%CuSO4/ 0.5%H2SO4, the test film by end surface grinding impregnates 20 hours in the boiling liquid）, observe the corrosion condition near welding heat affected zone.
Fig. 2 is the optical microscope photograph for the observation example for representing the test film section after sulfuric acid-copper sulphate corrosion test.As shown in the photo, the evaluation to welding heat affected zone is as follows, i.e., intercrystalline corrosion will be can confirm that, and then can see that the situation of the corrosion of very deep hole shape is evaluated as C, it can confirm that situation about corroding a little is evaluated as B, the situation that corrosion is not confirmed in the observation of light microscope is evaluated as A.In addition, being observed in whole total length the surface state after hot-roll annealing plate pickling.Using relative to total length, be able to observe that the ratio of the length of surface defect caused by crackle of steel billet or field trash as index, the ratio for occurring defect is evaluated as a for less than 3%, b is evaluated as more than 3% and less than or equal to 30%, c is evaluated as more than 30%.These results are shown in table 2.
As a result, within the scope of the invention as No.1 ~ 5 of example of the present invention, in 10 ~ 13,15, the corrosion resistance of weld part is good, and surface state is also extremely good.On the other hand, it is few in the martensite growing amount of welding heat affected zone in the F values disengaging scope of the invention as in the No.9 of comparative example and 14, therefore resistance to intergranular corrosion is substantially poor.In addition, in No.7,8,9 and 14 as comparative example departed from the scope of the present invention as No.6 the and FFV values of comparative example in Si higher than the scope of the present invention and Al less than the scope of the present invention, in surface observation after hot-roll annealing, it can largely observe that steel billet cause crackle, field trash cause scab.
Steel of the present invention can be used with the state of hot rolled plate or hot-roll annealing plate, therefore, and the generation scabbed can make yield rate decline to a great extent.This is due to that the portion of scabbing not only makes apparent variation, can also turn into the starting point become rusty, therefore as object part must be cut off during product export.
Claims (6)
1. a kind of structure stainless steel plate, it is characterised in that in terms of quality %, contain：C：0.01~0.03%, N：0.01~0.03%, Si：0.10~0.40%, Mn：1.5~2.5%, P：Less than 0.04%, S：Less than 0.02%, Al：0.05~0.15%, Cr：10~13%, Ni：0.5~1.0%, Ti：4 × (C+N)~0.3%, wherein, C, N represent the content in terms of quality % of these elements,
Also, it is defined to V：Less than 0.05%, Ca：Less than 0.0030%, O：Less than 0.0080%,
Moreover, the F values and FFV values that are represented with following formula meet F value≤11,5.0≤FFV value≤9.0, remainder is made up of Fe and inevitable impurity；
Also, mother metal portion in terms of volume fraction more than 50% is ferritic structure,
F values=Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 × (C+N)
FFV values=Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 × (Ni+Cu) -40 × (C+N)+20 × V
Wherein, in these formulas, each element symbol is the content in terms of quality % of these elements.
2. a kind of structure stainless steel plate, wherein, on the basis of the composition of claim 1, in terms of quality %, also contain Cu：Less than 1.0%.
3. a kind of structure stainless steel plate, wherein, on the basis of the composition of claim 1 or 2, in terms of quality %, also contain Mo：Less than 1.0%.
4. a kind of manufacture method of structure stainless steel plate, it is characterized in that, after the temperature of heating steel billet to 1100~1300 DEG C, hot rolling is carried out in the temperature province more than 1000 DEG C, or, after the hot rolling is carried out, hot rolled plate do not annealed or implement pickling after being annealed at a temperature of 600~1000 DEG C, wherein, is included in the hot rolling at least carry out hot roughing of the reduction ratio of more than 1 time for more than 30% rolling
The steel billet has consisting of, i.e. in terms of quality %, contain：C：0.01~0.03%, N：0.01~0.03%, Si：0.10~0.40%, Mn：1.5~2.5%, P：Less than 0.04%, S：Less than 0.02%, Al：0.05~0.15%, Cr：10~13%, Ni：0.5~1.0%, Ti：4 × (C+N)~0.3%, wherein, C, N represent the content in terms of quality % of these elements,
Also, it is defined to V：Less than 0.05%, Ca：Less than 0.0030%, O：Less than 0.0080%,
Moreover, the F values and FFV values that are represented with following formula meet F value≤11,5.0≤FFV value≤9.0, remainder is made up of Fe and inevitable impurity；
Also, mother metal portion in terms of volume fraction more than 50% is ferritic structure,
F values=Cr+2 × Si+4 × Ti-2 × Ni-Mn-30 × (C+N)
FFV values=Cr+3 × Si+16 × Ti+Mo+2 × Al-2 × Mn-4 × (Ni+Cu) -40 × (C+N)+20 × V
Wherein, in these formulas, each element symbol is the content in terms of quality % of these elements.
5. a kind of manufacture method of structure stainless steel plate, wherein, on the basis of the composition of the steel billet of claim 4, in terms of quality %, also contain Cu：Less than 1.0%.
6. a kind of manufacture method of structure stainless steel plate, wherein, on the basis of the composition of the steel billet of claim 4 or 5, in terms of quality %, also contain Mo：Less than 1.0%.
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| JP2010-124059 | 2010-05-31 | ||
| PCT/JP2011/062640 WO2011152475A1 (en) | 2010-05-31 | 2011-05-26 | Structural stainless steel sheet having excellent corrosion resistance in welded part, and method for producing same |
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| WO2015064077A1 (en) | 2013-10-31 | 2015-05-07 | Ｊｆｅスチール株式会社 | Ferrite-martensite two-phase stainless steel, and method for producing same |
| WO2015064128A1 (en) | 2013-10-31 | 2015-05-07 | Ｊｆｅスチール株式会社 | Ferrite-martensite two-phase stainless steel exhibiting low-temperature toughness, and method for producing same |
| CN108690936B (en) * | 2018-06-13 | 2020-12-01 | 燕山大学 | Stainless steel rail material for welding high manganese steel frog and rail and preparation method thereof |
| KR102173277B1 (en) * | 2018-11-06 | 2020-11-03 | 주식회사 포스코 | Hot-rolled steel sheet with excellent low temperature impact toughness and manufacturing method thereof |
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| US3650731A (en) * | 1969-01-31 | 1972-03-21 | Allegheny Ludlum Steel | Ferritic stainless steel |
| SU595420A1 (en) * | 1976-12-06 | 1978-02-28 | Предприятие П/Я А-1147 | Steel |
| JPS6199628A (en) * | 1984-10-19 | 1986-05-17 | Kawasaki Steel Corp | Manufacture of austenitic stainless steel sheet or strip |
| JPH03249150A (en) * | 1990-02-27 | 1991-11-07 | Nippon Steel Corp | Ferritic stainless steel having excellent toughness in weld zone |
| SU1723191A1 (en) * | 1990-06-25 | 1992-03-30 | Волгоградский Политехнический Институт | Stainless steel |
| JP2000080416A (en) * | 1998-08-31 | 2000-03-21 | Kawasaki Steel Corp | MANUFACTURE OF HIGH Cr MARTENSITIC WELDED STEEL PIPE FOR LINE PIPE EXCELLENT IN WELDABILITY AND CORROSION RESISTANCE |
| JP3508698B2 (en) * | 2000-06-06 | 2004-03-22 | Ｊｆｅスチール株式会社 | Stainless steel hot rolled steel strip for civil and building structures with excellent initial rust resistance |
| KR100765661B1 (en) * | 2000-08-31 | 2007-10-10 | 제이에프이 스틸 가부시키가이샤 | Low carbon martensitic stainless steel and production method thereof |
| JP2002121652A (en) * | 2000-10-12 | 2002-04-26 | Kawasaki Steel Corp | Cr-CONTAINING STEEL FOR AUTOMOBILE SUSPENSION |
| JP4457492B2 (en) | 2000-11-29 | 2010-04-28 | Ｊｆｅスチール株式会社 | Stainless steel with excellent workability and weldability |
| MXPA06000764A (en) * | 2003-07-22 | 2006-04-18 | Sumitomo Metal Ind | Martensitic stainless steel. |
| JP2006219717A (en) * | 2005-02-09 | 2006-08-24 | Nippon Steel Corp | Steel sheet for vessel having superior deformation resistance, surface characteristic and weldability, and manufacturing method therefor |
| JP4740021B2 (en) * | 2006-04-20 | 2011-08-03 | 新日鐵住金ステンレス株式会社 | Cr-containing thin steel sheet having excellent shape freezing property and method for producing the same |
| JP5225620B2 (en) * | 2006-07-04 | 2013-07-03 | 新日鐵住金ステンレス株式会社 | Low chromium-containing stainless steel excellent in corrosion resistance of heat-affected zone multiple times and its manufacturing method |
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