CN104471092A - Ferrite-austenite 2-phase stainless steel plate having low in-plane anisotropy and method for producing same - Google Patents
Ferrite-austenite 2-phase stainless steel plate having low in-plane anisotropy and method for producing same Download PDFInfo
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Abstract
This ferrite austenite 2-phase stainless steel plate comprises, by mass%, C: 0.001-0.10%, Si: 0.01-1.0%, Mn: 2-10%, P <u><</u> 0.05%, Ni: 0.1-3.0%, Cr: 15.0-30.0%, and N: 0.05-0.30%, with the remainder being Fe and inevitable impurities. The austenite phase percentage is 40-90% by surface area percentage, the maximum strength of the crystal orientation of the ferrite phase is 10 or less, and the hardness ratio of the austenite phase to the ferrite phase is 1.1 or greater.
Description
Technical field
The present invention relates to the little two-phase stainless steel plate be made up of mutually ferritic phase and austenite of the anisotropy that adds man-hour and manufacture method thereof.
The Patent 2012-52876 CLAIM OF PRIORITY that the application filed an application in Japan based on March 9th, 2012, and by its content quotation in this.
Background technology
Thus the two-phase stainless steel plate corrosion resistance excellent be made up of mutually ferritic phase and austenite and be micro organization is high strength, and excellent in fatigue characteristics, be used in chemical plant etc. widely.But the ductility of two-phase stainless steel plate is lower than austenite stainless steel, therefore sometimes crack when press forming, require to promote processibility.
As representational duplex stainless steel in the past, with SUS329J4L (25%Cr-7%Ni-3%Mo-0.1%N) for representative contains high Ni, Mo.But, develop recently and reduce Ni amount or the province's alloy ferritic-austenitic duplex stainless steel not containing Mo, be just used in various field (such as with reference to patent documentation 1).Containing like this economizes in Ni, Mo steel, by adding Mn or N, adjust the Ovshinsky scale of construction or guarantee solidity to corrosion, expecting that the steel that this contains province Ni, Mo can be used as substituting of SUS304 (18%Cr-8%Ni) or SUS316 (18%Cr-10%Ni-2%Mo).
On the other hand, when sheet metal forming being processed into different shape, being applied to various parts, press formability becomes problem.The index being called intra-face anisotropy is had in this press formability.When intra-face anisotropy is large, by the fretful problem of the part being called ear (namely ear processed (earing) becomes large problem) that is non-constant for the shape of the flange remainder producing molding or molding end.When producing this problem, yield rate during shaping is significantly deteriorated, and easily produces the ununiformity of the shape of molding, and therefore preferably intra-face anisotropy is little.
Described in non-patent literature 1, the intra-face anisotropy of Austenite and ferriteaustenite double phases of stainless steel plate is very big, has problems in steel-sheet plasticity.In addition, intra-face anisotropy is herein the intra-face anisotropy of r value, with the Δ r represented by following formula (1) for index.
Δ r=| (r
0+ r
90)/2-r
45| formula (1)
Wherein, the r in formula (1)
0the r value in the direction parallel relative to rolling direction, r
90be the r value of right angle orientation relative to rolling direction, r
45be the r value in 45 ° of directions relative to rolling direction.These r values are Lankford value (plastic strain ratios), and the method being basis in order to JIS Z2254 measures.Δ r refers to time large that intra-face anisotropy is large, therefore preferably less by above-mentioned viewpoint Δ r value.
In patent documentation 1, disclose and directly the molten steel of Austenite and ferriteaustenite double phases of stainless steel is carried out thin plate casting, manufacture the method without anisotropic steel plate of the mechanical properties indifference of rolling direction and width.This is the method omitted hot rolling, directly manufactured thin plate by molten steel, and the common manufacture method that through hot rolling manufacture such from the present invention is different.In addition, patent documentation 1 is the technology reducing the intensity of rolling direction and width or the difference of elongation, the technology of the intra-face anisotropy about r value not as the present invention.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 1-53705 publication
Non-patent literature
Non-patent literature 1:Materials Transactions, Vol.51, No.4 (2010) pp.644
Summary of the invention
The problem that invention will solve
Problem of the present invention is: the crystalline orientation intensity being conceived to ferritic phase especially, provides a kind of the Austenite and ferriteaustenite double phases of stainless steel plate that intra-face anisotropy is little, press formability is excellent and manufacture method thereof of r value.
For the means of dealing with problems
In order to solve above-mentioned problem, the present inventor etc. have investigated the r value of two-phase stainless steel plate and the manifesting property of intra-face anisotropy thereof in minute detail.And carry out various research repeatedly for reaching object like this, result obtains following experience.
Ferritic phase and austenite mix the r value of the duplex stainless steel of existence mutually and intra-face anisotropy is driven by the crystalline orientation intensity (texture) of ferritic phase.Herein, crystalline orientation intensity is the diffracted intensity measured by X-ray diffraction method, specifically, is the ratio of the diffracted intensity of the diffracted intensity relative to random sample.Therefore, crystalline orientation intensity be relative to crystal be oriented to random time (non-oriented crystal) the ratio of diffracted intensity of diffracted intensity, represent the degree of orientation.Crystalline orientation intensity is also referred to as the X-ray random strength ratio of specific crystalline orientation.In duplex stainless steel in the past, ferritic crystallization is upper significantly flourishing at the crystalline orientation (rolling orientation) parallel with rolling direction.Therefore, maximum strength (maximum value of the crystalline orientation intensity) grow of the crystalline orientation of sheet.Now, the r value of specific direction (be about 45 ° relative to rolling direction) uprises, the r value step-down of rolling direction or width.On the other hand, by adjusting component and method for making, can reduce cold rolling after cold-reduced sheet and the maximum strength of crystalline orientation of goods, realize the reduction of intra-face anisotropy.Specifically, by reducing Ni amount, and improving the amount of N or Mn, making the 2nd phase and austenite phase hardening, and making point rate optimization of austenite phase.Thus, the maximum strength that can reduce the crystalline orientation of ferritic phase in cold-rolled process is found.Now, find that the cold rolling draft of adjustment and annealing temperature are effective, that is, new discovery can reduce the maximum strength of the crystalline orientation of ferritic phase in cold-rolled process.In addition, in annealing afterwards, the maximum strength of crystalline orientation also can be realized to be maintained at little value.By more than, the goods that the intra-face anisotropy of material characteristic r value is little can be provided as.
The present invention completes based on above-mentioned experience, and the main idea of this invention is as follows.
(1) the Austenite and ferriteaustenite double phases of stainless steel plate that intra-face anisotropy is little, is characterized in that, in mass %, contains:
C：0.001～0.10％、
Si：0.01～1.0％、
Mn：2～10％、
P≤0.05％、
Ni：0.1～3.0％、
Cr:15.0 ~ 30.0% and
N：0.05～0.30％，
Remainder comprises Fe and inevitable impurity;
Austenite one after another counts 40 ~ 90% with area occupation ratio, and the maximum strength of the crystalline orientation of ferritic phase is less than 10, and austenite is more than 1.1 relative to the hardness ratio of ferritic phase.
(2) the Austenite and ferriteaustenite double phases of stainless steel plate that the intra-face anisotropy recorded of above-mentioned (1) or (2) is little, is characterized in that, in mass %, further containing being selected from
Mo：0.1～1.0％、
Cu：0.1～3.0％、
B：0.0005～0.0100％、
Al：0.01～0.5％、
Ti：0.005～0.30％、
Nb：0.005～0.30％、
Zr：0.005～0.30％、
Sn：0.05～0.50％、
W：0.1～2.0％、
Mg:0.0002 ~ 0.0100% and
More than a kind in Ca:0.0005 ~ 0.0100%.
(3) the Austenite and ferriteaustenite double phases of stainless steel plate that the intra-face anisotropy recorded of above-mentioned (1) or (2) is little, is characterized in that, as intra-face anisotropy index be less than 0.5 with the Δ r that following formula (1) represents,
Δ r=| (r
0+ r
90)/2-r
45| formula (1)
Wherein, r
0the r value in the direction parallel relative to rolling direction, r
90be the r value of right angle orientation relative to rolling direction, r
45be the r value in 45 ° of directions relative to rolling direction.
(4) manufacture method of the Austenite and ferriteaustenite double phases of stainless steel plate that a kind of intra-face anisotropy is little, it is characterized in that, it has following operation: carry out cold rolling operation by having the Austenite and ferriteaustenite double phases of stainless steel that the one-tenth above-mentioned (1) or (2) recorded is grouped into, and annealing operation afterwards;
In described cold rolling operation, draft is set as less than 90%,
In described annealing operation, annealing temperature is set as 1000 ~ 1100 DEG C, by until the speed of cooling of 500 DEG C is set as more than 5 DEG C/sec, keeps more than 5 seconds in the humidity province of 400 ~ 500 DEG C of process of cooling.
Invention effect
In the past, the intra-face anisotropy of Austenite and ferriteaustenite double phases of stainless steel plate was large, had problems in press formability.On the other hand, according to a form of the present invention, the steel sheet of the little Austenite and ferriteaustenite double phases of stainless steel plate of intra-face anisotropy can be obtained.By the Austenite and ferriteaustenite double phases of stainless steel plate of a form of the present invention being used as shaping purposes in the various fields such as household electrical appliances, building, automobile, larger effect can be obtained in the cost degradation etc. of environmental cure or parts.
Accompanying drawing explanation
Fig. 1 represents the texture of steel of the present invention and comparative steel and the figure of intra-face anisotropy (Δ r).
Fig. 2 is the figure of the maximum strength of the crystalline orientation representing ferritic phase and the relation of intra-face anisotropy (Δ r).
Fig. 3 is the figure of the relation representing austenite one after another (γ one after another) and intra-face anisotropy (Δ r).
Fig. 4 is the figure of the relation representing cold rolling draft and intra-face anisotropy (Δ r).
Embodiment
Below, present embodiment is explained.
First, the restriction reason of the chemical composition of the Austenite and ferriteaustenite double phases of stainless steel plate of present embodiment is described.Herein, the unit " % " of the content of composition refers to quality %.
When C amount is greater than 0.10%, plasticity and solidity to corrosion are deteriorated significantly, therefore the upper limit that C measures are set to 0.10%.C Absorbable organic halogens ground generates austenite phase, is the element of necessity for increasing the difference of hardness of austenite phase with ferritic phase, suppressing crystalline orientation intensity to rise.When C amount is less than 0.001%, be difficult to obtain duplex structure.Therefore, preferably the lower limit that C measures is set to 0.001%.In addition, when considering refining cost, weldability, C amount is preferably 0.02 ~ 0.05%.
Si is also as the useful element of reductor, but when Si amount is greater than 1.0%, hot workability deterioration, becomes and be difficult to manufacture.Therefore, Si amount is set to less than 1.0%.But in order to deoxidation, the Si of more than 0.01% is necessary, therefore the lower limit that Si measures is set to 0.01%.In addition, when considering refining cost, scale resistance, solidity to corrosion, Si amount is preferably 0.3% ~ 0.8%.
Mn is the element added as reductor.In addition, in order to stably generate austenite phase, increasing the difference of hardness of austenite phase and ferritic phase, to suppress the rising of the maximum strength of crystalline orientation, adding the Mn of more than 2%.When Mn amount is greater than 10%, solidity to corrosion is deteriorated significantly, therefore the upper limit that Mn measures is set to 10%.In addition, consider scale resistance or manufacture time pickling time, Mn amount be preferably 3.0 ~ 6.0%.
P contains as impurity, makes hot workability deterioration during manufacture, therefore the upper limit that P measures is set to 0.05%.But exceedingly reduce P amount and refining cost can be caused to increase, therefore P amount is preferably 0.02 ~ 0.04%.
Ni be Absorbable organic halogens generate the element of austenite phase, the lower limit that Ni measures is set to 0.1%.But, because cost of alloy is high, the upper limit that Ni measures is set to less than 3.0%.But exceedingly reduce Ni amount and sometimes cause solidity to corrosion deterioration, therefore Ni amount is preferably 0.5 ~ 3.0%.
For guaranteeing solidity to corrosion or scale resistance, add the Cr of more than 15.0%.On the other hand, add a large amount of Cr and cost of alloy can be caused to increase, therefore the upper limit that Cr measures is set to 30.0%. in addition, considers manufacturing, Cr amount is preferably 17.0 ~ 25.0%.
N can promote the solidity to corrosion of duplex stainless steel.In addition, N Absorbable organic halogens ground generates austenite phase, increases the difference of hardness of austenite phase and ferritic phase, suppresses the rising of the maximum strength of crystalline orientation.Therefore, the N of more than 0.05% is added.On the other hand, when N amount is greater than 0.30%, remarkable hardening, and castibility or hot workability are deteriorated.Therefore, the upper limit that N measures is set to 0.30%.In addition, consider and suppress the texture of weldability or ferritic phase towards particular crystal orientation prosperity, N amount is preferably 0.10 ~ 0.30%.N amount is more preferably greater than 0.15% and is less than or equal to 0.30%.
Mo is the element contributing to promoting solidity to corrosion or hot strength, also can add the Mo of more than 0.1% as required.When Mo amount is less than 0.1%, the effect of solidity to corrosion and the hot strength of can not getting a promotion fully.But Mo generates ferritic element, when therefore Mo amount is greater than 1.0%, austenite phase can not be generated fully.Therefore, Mo amount is set to 0.1 ~ 1.0%.When considering cost of alloy or manufacturing, Mo amount is preferably 0.1 ~ 0.5%.
For controlling the one after another of solidity to corrosion or austenite phase, the Cu of 0.1 ~ 3.0% also can be added as required.When Cu amount is less than 0.1%, can not get a promotion corrosion proof effect fully.When Cu amount is greater than 3.0%, promote corrosion proof effect saturated, and suppress the effect of the one after another of austenite phase also saturated.When considering hot workability, Cu amount is preferably 0.1 ~ 2.0%.
B is at grain boundary segregation, the element promoting hot workability, also can add the B of more than 0.0005% as required.When B amount is less than 0.0005%, the effect of the hot workability that can not get a promotion fully.But B generates ferritic element, when therefore B amount is greater than 0.0100%, austenite phase can not be generated fully.Therefore, B amount is set to 0.0005 ~ 0.0100%.In addition, when considering grain boundary corrosion, B amount is preferably 0.0005 ~ 0.0030%.
Al fully can be used as reductor.In addition, Al can promote scale resistance or solidity to corrosion.Therefore, the Al of 0.01 ~ 0.5% can also be added as required.When Al amount is less than 0.01%, the scale resistance that can not get a promotion fully or corrosion proof effect.Al amount is when being greater than 0.5%, promote scale resistance or corrosion proof effect saturated.When considering toughness, Al amount is preferably 0.01 ~ 0.10%.
Ti makes the miniaturization of organizing of weld part and cast structure be effective element for forming TiN with N.In addition, Ti promotes corrosion proof element.Therefore, the Ti of 0.005 ~ 0.30% can also be added as required.When Ti amount is less than 0.005%, the effect organizing miniaturization by weld part and cast structure can not be shown fully.When Ti amount is greater than 0.30%, this effect is saturated, and in the manufacturing process of steel plate, become the reason producing surface imperfection.When considering cost of alloy or toughness, Ti amount is preferably 0.005 ~ 0.15%.
Nb is the element having the effect similar with Ti and promote intensity, also can add the Nb of 0.005 ~ 0.30% as required.When Nb amount is less than 0.005%, the effect organizing miniaturization by weld part and cast structure can not be shown fully.When Nb amount is greater than 0.30%, this effect is saturated.When considering cost of alloy or toughness, Nb amount is preferably 0.005 ~ 0.15%.
Zr is also the element having the effect similar with Ti or Nb and promote scale resistance, also can add the Zr of 0.005 ~ 0.30% as required.When Zr amount is less than 0.005%, the effect organizing miniaturization by weld part and cast structure can not be shown fully, the effect promoting scale resistance can not be shown fully.When Zr amount is greater than 0.30%, this effect is saturated.When considering cost of alloy or toughness, Zr amount is preferably 0.005 ~ 0.15%.In addition, when Zr amount is greater than 0.15%, the tendency that flexible declines.
Sn promotes corrosion proof element, also can add the Sn of 0.05 ~ 0.50% as required.When Sn amount is less than 0.05%, can not shows fully and promote corrosion proof effect.When Sn amount is greater than 0.50%, this effect is saturated.When considering hot workability or weldability, Sn amount is preferably 0.05 ~ 0.20%.
W is the element promoting solidity to corrosion or thermotolerance, also can add the W of 0.1 ~ 2.0% as required.When W amount is less than 0.1%, the effect promoting solidity to corrosion or thermotolerance can not be shown fully.When W amount is greater than 2.0%, this effect is saturated.When considering cost of alloy or toughness, W amount is preferably 0.1 ~ 1.0%.
Mg is the element made full use of as reductor.In addition, Mg organizes the effective element of miniaturization to weld part and cast structure.Therefore, the Mg of 0.0002 ~ 0.0100% can also be added as required.When Mg amount is less than 0.0002%, the effect organizing miniaturization by weld part and cast structure can not be shown fully.When Mg amount is greater than 0.0100%, this effect is saturated.When considering manufacturing, Mg amount is preferably 0.0002 ~ 0.0020%.
Ca and S combines can promote hot workability, therefore also can add the Ca of 0.0005 ~ 0.0100% as required.When Ca amount is less than 0.0005%, the effect promoting hot workability can not be shown fully.When Ca amount is greater than 0.0100%, this effect is saturated.When considering solidity to corrosion, Ca amount is preferably 0.0005 ~ 0.0100%.
Then, the main points of present embodiment and the crystalline orientation intensity of ferritic phase are described.
By rolling and thermal treatment, the crystallization of ferritic phase and austenite phase is flourishing in particular crystal orientation.Steel plate characteristic is affected in the crystallization of particular crystal orientation prosperity.Degree (degree of orientation) towards particular crystal orientation prosperity is proportional with the crystalline orientation intensity measured by X-ray diffraction method, neutron diffraction method etc.Herein, crystalline orientation intensity is the ratio of the diffracted intensity of diffracted intensity relative to random sample, also referred to as the X-ray random strength ratio of particular crystal orientation.The mensuration of crystalline orientation intensity has many kinds of methods, but specifies the crystalline orientation intensity that obtained by X-ray diffraction method in present embodiment.Figure l represents the texture of the ferritic phase of the two-phase stainless steel plate (steel of the present invention and comparative steel) with different intra-face anisotropy.These two-phase stainless steel plates to be thickness be 1.0mm cold rolling-annealed sheet, be cold rolling draft be 78%, annealing temperature manufactures under being the condition of 1050 DEG C and obtains.Texture measured by the following method.First, mechanical mill and electrolytic polishing are implemented to steel plate, shows the central zone of thickness of slab.Use X-ray diffraction device (Liue electrical machinery Industrial Co., Ltd's system), and use Mo-K α line, measure the positive pole graph of (200), (310) and (211) of thickness of slab central zone.Use spherical harmonic function method by these positive pole graphs, obtain 3 dimension crystalline orientation density functions.
Figure l is the 3 dimension texture represented by Bunge method, is the cross section (φ 2=45 ° cross section) can finding out crystalline orientation intensity with level line.Herein, crystalline orientation intensity is the ratio of the diffracted intensity of diffracted intensity relative to random sample.In figure l, the crystalline orientation (rolling orientation) being parallel to the ferritic phase of rolling direction is { 100}<011>, { 211}<011>.In the texture of the comparative steel of Fig. 1, crystallization the rolling orientation as ferritic phase { 100}<011>, { 211}<011> orientation is flourishing significantly, and the maximum strength (maximum value of crystalline orientation intensity) of crystalline orientation is up to 18.In addition, the Δ r of the intra-face anisotropy of display r value is up to 1.34, and press formability is poor.
On the other hand, in the texture of the steel of the present invention of Fig. 1, the prosperity towards the crystallization in the rolling orientation is suppressed, and the maximum strength (maximum value of crystalline orientation intensity) of crystalline orientation is 8, lower than comparative steel.In addition, Δ r is 0.38, and known anisotropy is little.By above result, the intra-face anisotropy of known r value is driven by the texture of the ferritic phase as parent phase, and by suppressing the prosperity of specific texture effectively can reduce anisotropy.Fig. 2 represents the maximum strength of the crystalline orientation of ferritic phase and the relation of Δ r.When maximum strength is less than 10, Δ r is less than 0.5.Therefore, in present embodiment, the maximum strength of the crystalline orientation of ferritic phase is defined as less than 10.The lower value of the maximum strength of the crystalline orientation of ferritic phase is 1 of random state.Δ r is preferably lower, but when Δ r is less than 0.5, can not produce the problem relevant to shape when suppressing.Therefore, in present embodiment, Δ r is defined as less than 0.5.Δ r more preferably less than 0.4.
In addition, the maximum strength of crystalline orientation is the maximum value in the crystalline orientation intensity of whole crystalline orientation.Measure the positive pole graph of (200), (310) and (211), when obtaining 3 dimension crystalline orientation density function by these 3 positive pole graphs, the information of the crystalline orientation intensity about whole crystalline orientation can be obtained.
Intra-face anisotropy is the intra-face anisotropy of r value, with the Δ r represented by known following formula (1) for index.
Δ r=| (r
0+ r
90)/2-r
45| formula (1)
Wherein, the r in formula (1)
0the r value in the direction parallel relative to rolling direction, r
90be the r value of right angle orientation relative to rolling direction, r
45be the r value in 45 ° of directions relative to rolling direction.These r values are Lankford value (plastic strain ratios), and the method being basis in order to JIS Z2254 measures.Δ r refers to time large that intra-face anisotropy is large, therefore preferably less by above-mentioned viewpoint Δ r value.
In present embodiment, the austenite one after another (area occupation ratio) of Austenite and ferriteaustenite double phases of stainless steel is also for reducing the key element of intra-face anisotropy.Austenite is separated out in hot-rolled process as the 2nd, and its amount of precipitation is along with temperature variation.In the present embodiment, find following new technological thought: by the crystalline orientation intensity (texture) of cold rolling control ferritic phase, and cold rolling and annealing after also maintain this crystalline orientation characteristic (texture), low intra-face anisotropy can be shown.In the difference of hardness hour without austenite phase time or austenite phase and ferritic phase, by rolling deformation, the particular crystal orientation of ferritic phase sharply flourishing (prosperity of rolling texture).Now, even if by thermal treatment afterwards, the maximum strength also grow (prosperity of recrystallization texture) of crystalline orientation.
On the other hand, when the steel of present embodiment forms, the ferritic phase of parent phase is mutually more soft than the austenite of the 2nd phase.Therefore, in cold rolling process, be subject to by roller being out of shape under the state that limits time, ferritic phase is subject to extremely uneven distortion mutually from the austenite of hard.The present inventor etc. measure the hardness of austenite phase and ferritic phase in detail with Using Nanoindentation.Found that, when the hardness of austenite phase is more than 1.1 times of the hardness of ferritic phase, anisotropy diminishes.The ferritic phase of uneven strain to parent phase is imported in large quantities mutually from the austenite of hard, therefore local and produce crystalline orientation unevenly and rotate in deformation process.Therefore, think that the prosperity of particular crystal orientation is suppressed, anisotropy diminishes thus.In order to make little intra-face anisotropy stabilization, austenite is preferably more than 1.2 relative to the hardness ratio of ferritic phase.When hardness ratio is greater than 2.0, becomes the state that austenite hardens mutually significantly, crack at the interface of ferritic phase with austenite phase during formed machining.Therefore, the upper limit of hardness ratio is preferably 2.0.
In addition, the present inventor etc. have also investigated austenite one after another (point rate (Line Integral rate) of austenite phase).Prepare the cold-reduced sheet with the composition identical with the steel of the present invention of Fig. 1, in 950 DEG C ~ 1150 DEG C adjustment annealing temperatures, make the sample with various austenite one after anothers.In addition, in order to make austenite one after another change, the annealing temperature of cold-reduced sheet is made to fade to 1150 DEG C from 950 DEG C.Measure austenite one after another and the Δ r of the sample obtained.Herein, austenite one after another ferrite survey meter measures, but also tries to achieve by image analysis apparatus or EBSP resolver etc.With the austenite one after another of the sample made by the annealing temperature of 1100 DEG C for 40%.With the austenite one after another of the sample made by the annealing temperature of 1000 DEG C for 90%.
Fig. 3 represents the relation of austenite one after another and intra-face anisotropy (Δ r).As shown in Figure 3, when austenite one after another is below more than 40% 90%, Δ r is less than 0.5.Therefore, the lower limit of austenite one after another is set to 40%, and the upper limit is set to 90%.Discovery like this, reduces intra-face anisotropy, and makes the effect of little intra-face anisotropy stabilization also by austenite one after another (Line Integral rate) impact.When austenite one after another exceedingly increases, will be subject to the excessive uneven distortion from austenite phase in cold-rolled process, the texture of the ferritic phase after cold rolled annealed is flourishing.Therefore, think that anisotropy becomes large.Therefore, austenite one after another is set to 40 ~ 90%.Stably reduce intra-face anisotropy further, and when considering intensity or ductility, austenite one after another is preferably 50 ~ 80%, more preferably 60 ~ 80%.
Then, manufacture method is described.
The manufacture method of the steel plate of present embodiment is made up of each operation of steel-hot rolling-pickling-cold rolling-annealing-pickling processed.In steel processed, be preferably used in the steel of composition that melting in converter or electric furnace contains aforementioned essential component and adds as required, then carry out the method for 2 refinings.Molten steel after melting is made slab according to known castmethod (continuous casting).By heating of plate blank to the temperature specified, and be rolled into the thickness of slab of regulation with continuous rolling.In hot rolling, carry out rolled slab with the hot rolls be made up of multiple rolling stand, then batch.In present embodiment, and not specially provided for casting and hot-rolled condition, suitably select according to composition.
After hot rolling, hot-rolled sheet annealing can be implemented and also can omit, carry out cleanup acid treatment, implement cold rolling afterwards.In cold rolling, cold rolling draft is set to less than 90%.Fig. 4 represents the relation of draft and Δ r.When draft is greater than 90%, Δ r is greater than 0.5, and intra-face anisotropy becomes large.When excessive strain ground in cold rolling becomes large, the maximum strength of the crystalline orientation of ferritic phase sharply increases (in rolling orientation, crystallization is flourishing significantly).Think that intra-face anisotropy becomes large thus.In addition, when considering ductility or productivity, cold rolling draft is preferably 30 ~ 80%.And not specially provided for cold rolling in other conditions (roller footpath, road number of times, rolling temperature etc.), suitably select according to productivity.
Annealing after cold rolling is implemented in order to adjust austenite one after another.In order to austenite one after another is set to more than 40%, the Heating temperature of annealing is set to less than 1100 DEG C.In order to austenite one after another is set to less than 90%, the Heating temperature of annealing is set to more than 1000 DEG C.But instead the annealing under excessive high temperature make austenite one after another reduce, and makes coarsening.Therefore, the increase of the maximum strength of the crystalline orientation of ferritic phase is caused.Therefore, the Heating temperature (annealing temperature) of annealing is set to 1000 ~ 1100 DEG C.In addition, from the view point of ductility or toughness, annealing temperature is preferably 1020 ~ 1075 DEG C.In addition, when the speed of cooling after heating is crossed slow, Cr Carbonitride Precipitation in process of cooling, toughness or solidity to corrosion deterioration.Therefore, by until the speed of cooling of 500 DEG C is set to more than 5 DEG C/sec.When speed of cooling is greater than 500 DEG C/sec, plate profile is significantly deteriorated, therefore the upper limit of speed of cooling is set to 500 DEG C/sec.In addition, when considering productivity or pickling, speed of cooling is preferably 10 ~ 50 DEG C/sec, and method of cooling suitably can select vapor-water cooling, water cooling etc.
In order to make the hardness of austenite phase be 1.1 times of the hardness of ferritic phase, need to make N denseization in austenite, by austenite phase hardening.In present embodiment, keep more than 5 seconds in the humidity province of 400 ~ 500 DEG C of process of cooling.Thus, N denseization in austenite is made.But, when the hold-time is greater than 500 seconds, makes productivity deteriorated significantly, therefore the upper limit of hold-time be set to 500 seconds.In addition, when considering productivity, the hold-time is preferably less than 60 seconds.
For the manufacture method of other operations and not specially provided for, the thickness of hot-rolled sheet, the annealing atmosphere etc. of cold-reduced sheet suitably can be selected.In addition, cold rolling, annealing after also can invest skin-pass or pulling force leveling.In addition, the thickness of slab of goods also can be selected according to the thickness of required component (component after processing).
Embodiment
The steel becoming to be grouped into shown in melting table l, be cast as slab, hot rolling slab makes the coils of hot rolled that thickness is 3.5mm.Afterwards, by coils of hot rolled annealing, pickling, the draft with 78% is cold rolling makes cold-reduced sheet.Then, cold-reduced sheet is annealed.In annealing operation, cold-reduced sheet is heated to 1050 DEG C, then until the speed of cooling of 500 DEG C cools under being the condition of 10 DEG C/sec.After annealing, implement pickling and make sheet.With preceding method, Δ r, the maximum strength of crystalline orientation and the mensuration of austenite one after another have been carried out to the sheet of gained like this.
Table 3
The Austenite and ferriteaustenite double phases of stainless steel plate of steel No.1 ~ 10 has the composition of steel of the scope of present embodiment defined, and the maximum strength of the crystalline orientation of austenite one after another, ferritic phase meets the scope of present embodiment defined.In addition, the Δ r as anisotropy index is less than 0.5, and intra-face anisotropy is little.
On the other hand, steel No.11 is the steel being equivalent to SUS329J4L, and the amount of Ni and Mo departs from the scope of present embodiment defined.In addition, austenite one after another is low, and the maximum strength of the crystalline orientation of ferritic phase is high significantly.Therefore, Δ r is greater than 0.5, and anisotropy is large.
The N amount of the C amount of steel No.12, the Mn amount of steel No.14 and steel No.17 is fewer than the lower limit of the scope of present embodiment defined.C, Mn and N are austenite generting elements, and therefore the maximum strength of steel No.12, the austenite one after another of 14 and 17 and the crystalline orientation of ferritic phase is outside the scope of present embodiment defined.Therefore, Δ r is large.
The W amount of the Mo amount of the Si amount of steel No.13, the Cr amount of steel No.16, steel No.18, the B amount of steel No.20, the Al amount of steel No.21, the Sn amount of steel No.25 and steel No.26 is all many than the upper limit of the scope of present embodiment defined.Si, Cr, Mo, B, A1, Sn and W are ferrite generating elements, and therefore in steel No.13,16,18,20,21,25 and 26, ferrite one after another becomes many.Therefore, ferritic phase is flourishing in rolling orientation significantly, and Δ r is large.
The Ni amount of steel No.15 is measured more than the upper limit of the scope of present embodiment defined with the Cu of steel No.19.Ni and Cu is austenite generting element, and therefore in steel No.15,19, austenite one after another becomes too much, and the maximum strength of the crystalline orientation of ferritic phase is outside the scope of present embodiment defined.Therefore, Δ r is large.
The Zr amount of the Ti amount of steel No.22, the Nb amount of steel No.23 and steel No.24 is more than the upper limit of the scope of present embodiment defined.Therefore, in steel No.22 ~ 24, Ti, Nb and Zr are combined with C or N as austenite generting element, suppress austenitic generation, and austenite one after another declines.Therefore, Δ r is large.
Use the steel having the steel identical with steel No.1 ~ 4 of example of the present invention and form, the annealing conditions changing cold rolling draft and cold-reduced sheet, to manufacture steel curved beam, determines Δ r, crystalline orientation intensity and austenite one after another with preceding method.Obtained result is shown in table 4.
As shown in table 4, steel curved beam No.101 ~ 104 of example of the present invention manufacture under the condition of present embodiment defined.The Δ r of steel curved beam No.101 ~ 104 of these examples of the present invention is little, and intra-face anisotropy is little.Therefore, press formability is good.On the other hand, steel curved beam No.105 ~ 110 of comparative example manufacture under cold rolling draft, cold-reduced sheet annealing temperature and speed of cooling depart from the condition of the scope of present embodiment defined.The Δ r of steel curved beam No.105 ~ 110 of these comparative examples is large, and intra-face anisotropy is large.Therefore, have problems in press formability.
Utilizability in industry
The intra-face anisotropy of the r value of the Austenite and ferriteaustenite double phases of stainless steel plate of present embodiment is little, and press formability is excellent.Therefore, the Austenite and ferriteaustenite double phases of stainless steel plate of present embodiment is applicable to being used in the press forming product requiring excellent corrosion resistance.
Claims (4)
1. the Austenite and ferriteaustenite double phases of stainless steel plate that intra-face anisotropy is little, is characterized in that, in mass %, contains:
C：0.001～0.10％、
Si：0.01～1.0％、
Mn：2～10％、
P≤0.05％、
Ni：0.1～3.0％、
Cr:15.0 ~ 30.0% and
N：0.05～0.30％，
Remainder comprises Fe and inevitable impurity;
Austenite one after another counts 40 ~ 90% with area occupation ratio, and the maximum strength of the crystalline orientation of ferritic phase is less than 10, and austenite is more than 1.1 relative to the hardness ratio of ferritic phase.
2. the Austenite and ferriteaustenite double phases of stainless steel plate that intra-face anisotropy according to claim 1 is little, is characterized in that, in mass %, further containing being selected from
Mo：0.1～1.0％、
Cu：0.1～3.0％、
B：0.0005～0.0100％、
Al：0.01～0.5％、
Ti：0.005～0.30％、
Nb：0.005～0.30％、
Zr：0.005～0.30％、
Sn：0.05～0.50％、
W：0.1～2.0％、
Mg:0.0002 ~ 0.0100% and
More than a kind in Ca:0.0005 ~ 0.0100%.
3. the Austenite and ferriteaustenite double phases of stainless steel plate that intra-face anisotropy according to claim 1 and 2 is little, is characterized in that, as intra-face anisotropy index be less than 0.5 with the Δ r that following formula (1) represents,
Δ r=| (r
0+ r
90)/2-r
45| formula (1)
Wherein, r
0the r value in the direction parallel relative to rolling direction, r
90be the r value of right angle orientation relative to rolling direction, r
45be the r value in 45 ° of directions relative to rolling direction.
4. the manufacture method of the Austenite and ferriteaustenite double phases of stainless steel plate that an intra-face anisotropy is little, it is characterized in that, it has following operation: the Austenite and ferriteaustenite double phases of stainless steel be grouped into by the one-tenth had described in claim 1 or 2 carries out cold rolling operation, and annealing operation afterwards;
In described cold rolling operation, draft is set as less than 90%,
In described annealing operation, annealing temperature is set as 1000 ~ 1100 DEG C, by until the speed of cooling of 500 DEG C is set as more than 5 DEG C/sec, keeps more than 5 seconds in the humidity province of 400 ~ 500 DEG C of process of cooling.
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| PCT/JP2013/055945 WO2013133259A1 (en) | 2012-03-09 | 2013-03-05 | Ferrite-austenite 2-phase stainless steel plate having low in-plane anisotropy and method for producing same |
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| CN109355485A (en) * | 2018-11-19 | 2019-02-19 | 重庆大学 | A kind of preparation method of High-strength high-plasticity ferrite austenite dual phase steel |
| CN109440014A (en) * | 2019-01-14 | 2019-03-08 | 东北大学 | A kind of low chrome content, low nickel two phase stainless steel and preparation method thereof |
| CN109576591A (en) * | 2019-02-12 | 2019-04-05 | 鞍钢股份有限公司 | 700 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
| CN109628840A (en) * | 2019-02-12 | 2019-04-16 | 鞍钢股份有限公司 | 550 MPa-grade cold-rolled corrosion-resistant dual-phase steel and manufacturing method thereof |
| WO2024139542A1 (en) * | 2022-12-28 | 2024-07-04 | 广东省科学院新材料研究所 | High-strength corrosion-resistant anti-cracking steel, and preparation method therefor and use thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN104471092B (en) | 2018-01-02 |
| KR20140105849A (en) | 2014-09-02 |
| WO2013133259A1 (en) | 2013-09-12 |
| TW201348465A (en) | 2013-12-01 |
| JP2013185231A (en) | 2013-09-19 |
| JP5869922B2 (en) | 2016-02-24 |
| TWI519653B (en) | 2016-02-01 |
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