CN109136735A - Ferritic stainless steel and its manufacturing method with favorable forming property - Google Patents
Ferritic stainless steel and its manufacturing method with favorable forming property Download PDFInfo
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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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
- 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
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
Ferritic stainless steel and its manufacturing method with favorable forming property, its ingredient percent are as follows: C 0.002%~0.02%, N 0.002%~0.02%, Si 0.05%~0.60%, Mn 0.05%~0.50%, Cr 15.0%~19.0%, Ti 0~0.5%, Nb 0~0.6%, Zr:0~0.05%, Ta 0~0.04%, and meet
Description
Technical field
The present invention relates to ferritic stainless steel, in particular to a kind of ferritic stainless steel with favorable forming property and its
Manufacturing method.
Background technique
Stainless steel is due to its surface aesthetic, and excellent corrosion resistance is by extensively in building, household electrical appliance, kitchen article, vapour
Various aspects in the life such as vehicle exhaust, especially austenitic stainless steel, due to its high corrosion resistance and good forming
Performance is enough completely suitable for use above, therefore has been widely used.
Nevertheless, since, containing the nickel of high-content, the cost of nickel has accounted for austenite stainless in austenitic stainless steel
The 60-80% of steel, fluctuating widely for nickel valence have seriously affected the normal production and supply of stainless steel enterprises.With metallurgical industry
Progress and the practice of vast metallurgical industry person's many years, have been able to the key factor influence ferritic stainless steel formability:
To a lower level, ferritic stainless steel also has been widely used the control of carbon nitrogen gap atom.But in Ultra-low carbon
In nitrogen ferritic stainless steel production process, a series of problem is still remained, for example, deep drawability improves, brings ear processed therewith
Height increases, anti-impact pressure corrugation penalty after Ultra-low carbon nitridation.
For above problem, existing technology proposes many methods to improve the forming property of ferritic stainless steel.
In Chinese patent CN200580000342.2 patent, proposing reduces carbon nitrogen gap atom, and passes through the analysis of Nb in control steel
Out object in 0.05-0.6% content hereinafter, and control recrystallization rate 10-90% method obtain be more than 35% elongation percentage.
Although obtaining higher elongation percentage, in actual production, the precipitate of Nb is very tiny, and conventional Electronic Speculum equipment
It is difficult quantitative analysis, carrys out great difficulty to the out tape of patent.
In Chinese patent CN03814082.9, it is desirable that C (mass fraction), 0.05% < Ti < 0.5% below 0.01%
And N < 0.04%, 8 < Ti/ (C+N) < 30, it is main by controlling grain size at 6.0 grades or more, while titaniferous class is precipitated size and exists
Between 0.05 μm -1.0 μm, high r value and low yield strength are obtained.This patent mainly passes through individually addition Ti element, no
Nb containing stabilizing element.It is the same with above-identified patent, good processing performance is obtained by the control of precipitation size, in reality
Strict control is equally difficult in production.
In Chinese patent CN00800983.x patent, in the case where not pursuing ultra-low carbon nitrogen atom, it is added to V element
Meet: 0.06≤(C+N)≤0.12,1≤C/N, and then meet 1.5 × 10-3≤(V×N)≤1.5×10-2.Pass through ingredient
Control obtains lower corrugation height, and good deep drawability: for r value between 1.4-1.7, elongation percentage reaches 35%.
In Chinese patent CN200910075388.0 patent, too low interstitial atom is not pursued yet, and C is controlled in 0.02-
0.04%, by control hot-roll annealing temperature at 800-880 DEG C, keep the temperature 10-13 hours, and control cold-reduced sheet 860 DEG C ±
20 DEG C, finished product r value is more than 1.2, and Δ r value is less than 0.4, better than the deep drawability of commonsense method.
In Chinese patent CN98801478.5, interstitial atom is reduced, and by compound addition Nb, Ti and V, meets Nb+V
=0.05-0.1% and V/Nb:2-5.Define the heating temperature of slab at 1170 DEG C hereinafter, roughing end temp is at 950 DEG C
More than, high average r value and lower Δ r value thereby is achieved.Although obtaining good forming property, it is added to conjunction
Gold element V, and the additive amount of its Nb is not also high.
In Chinese patent CN200910163843.2, the annealing process of hot rolled plate is omitted, carries out 40% or more first
Once cold rolling, intermediate annealing is carried out at 750-900 DEG C, then carry out 60% or more final cold rolling, then in 750-
Final annealing is carried out at 1000 DEG C, reaches 50% or more by the area ratio of ± 10 ° of orientation crystal grain of control production board { 554 }.
In Chinese patent CN200810081327.0, the annealing process of hot rolled plate is equally omitted, carries out 40% first
Above once cold rolling carries out intermediate annealing at 850-1000 DEG C, then carries out 65% or more final cold rolling, then exists
Final annealing is carried out at 750-1000 DEG C, then controls the texture after the thin plate in 0 °, 45 ° and 90 ° three directions stretches 20%
Intensity ratio obtains good surface roughness.
Two above patent although by the optimization of metallurgical technology, and the crystal grain orientation for controlling final finished plate obtain compared with
Small surface roughness, but deep drawability is not directed to.
In Chinese patent CN98801478.5 patent, pass through the addition of niobium titanium stable composition element, Ti/N content ratio
Greater than 12, and the total content of Nb and V is determined less than 0.1% and V/Nb=2-5, while by hot rolling heating and temperature control 1170
DEG C hereinafter, completing rough rolling process at 950 DEG C or more.
In Chinese patent CN200910048291.0 patent, damage surface quality of continuously cast slab element ti is not added, is used
Single Nb stablizes ferritic stainless steel, forms niobium carbonitrides precipitated phase, and use high roughing temperature and low finishing temperature, thus
Eliminate the surface wrinkling of cold-reduced sheet.
Chinese patent CN200910220459.1 proposes a kind of hot rolling technology method for reducing corrugation height, mainly logical
1000 DEG C~1100 DEG C progress roughing, 700 DEG C~850 DEG C progress finish rolling of low temperature are crossed, this method makes the wrinkle of final finished plate
Pleat height reduces by 10~50%.
The above patent has carried out detailed discussion to punching performance and corrugation height, it is lower to obtain punching press r value, while again
Point has carried out corrugated control from hot rolling technology.
Summary of the invention
The purpose of the present invention is to provide a kind of ferritic stainless steel and its manufacturing method with favorable forming property, should
Ferritic stainless steel has high deep drawing quality (r value be greater than 1.7), low in-plane anisotropy (Δ r value is less than 0.3) and well resists
The features such as wrinkle property (corrugation height is less than 25 μm).
In order to achieve the above objectives, the technical scheme is that
Ferritic stainless steel with favorable forming property, ingredient percent are as follows:
C:0.002%~0.02%,
N:0.002%~0.02%,
Si:0.05%~0.60%,
Mn:0.05%~0.50%,
Cr:15.0%~19.0%,
Ti:0~0.5%,
Nb:0~0.6%,
Zr:0~0.05%,
Ta:0~0.04%,
Surplus is Fe and inevitable impurity, and is met,
Preferably, the deep drawability of the stainless steel is indicated with average plastic strain ratio r, and average r value is greater than 1.7, wherein
R=(r0+r90+2r45Tensile sample is processed into according to JIS5 standard in)/4, and measurement is parallel to the r value of rolling after stretching 15%:
r0, the r value at 45 ° with rolling direction: r45, perpendicular to the r value of rolling direction: r90；The evaluation of corrugation height: after pre-stretching 25%
The corrugation height Pt of production board, the difference in height of wave crest and trough are measured, Pt value is 25 μm or less.
Preferably, the marcotexture of the ferritic stainless steel, in the metal of body-centered cube BCC structure,It is knitted in the intensity that { 111 }<112>that Eulerian angles are (30 °, 55 °, 45 °) and (90 °, 55 °, 45 °) are orientated in section
The peak strength of structure is greater than 7.
Ferritic stainless steel in-plane anisotropy Δ r value of the present invention, general calculation formula are as follows: Δ r=(r0+
r90-2r45)/2 set its Δ r < 0.3.
In the ingredient design of steel of the present invention:
C: many disadvantages on ferrite stainless Steel Properties, such as: ductile-brittle transition temperature is high, and notch sensitivity is big, anti-corrosion
Property difference is all related with the carbon in steel.Therefore its content it is more fewer better, so by the upper limit be set as 0.02%, concurrently,
It will lead to the increase of refining cost to completely remove carbon in smelting process, therefore set its lower limit as 0.002%.
N: it is the same with C, will lead to the decline of stainless steel formability and corrosion resistance, thus its content be also it is more few more
Good, so its upper limit is set as 0.02%, but excessive reduction will lead to the drop of TiN particle when ferritic stainless steel solidifies
It is low, so as to cause the increase of column crystal content, the wrinkle resistance of thin plate, while the cost of the smelting considered, lower limit can be deteriorated
It is set as 0.002%.
Si: solution strengthening element, the increase of content will lead to the decline of elongation percentage and toughness, and the fewer content the better,
Its upper limit is set as 0.6%, but Si is added as deoxidant element sometimes, while considering smelting cost, lower limit set
It is 0.05%.
Mn: weak austenite former, while being also solution strengthening element, the illeffects of sulphur in steel can be inhibited,
But its content increase can deteriorate corrosive nature, therefore its content needs to control below 0.5%.
Cr: being the essential element for improving corrosion resistance, and the corrosion resistant in oxidizing acid can be remarkably reinforced in the increase of content
Corrosion, improves its anticorrosion stress-resistant in chloride solution, spot corrosion and crevice corrosion behavior, but the increase of its content meeting again
Lead to the reduction of toughness and processability, preferably 15-19%.
P and S: being harmful element, P is harmful for hot-workability, and S can be separated in crystal edge, and make crystal grain
Edge becomes fragile, and in addition the formation of MnS is also to the corrosion resistance of steel and its nocuousness.Therefore the content of P and S should be in existing steel making ability
On the basis of it is relatively low as far as possible.
Nb, Ti, Zr and Ta: suitable niobium, titanium can make the carbon of chromium, nitride in stainless steel transfer to be formed titanium, niobium carbon,
The crystal grain of nitride and fining ferrite stainless steel, improves the intergranular corrosion resistance performance of ferritic stainless steel.Suitable titanium in steel
And nitrogen, moreover it is possible to which fining ferrite seam organization improves plastic property of weld bead and formability, and furthermore TiN begins to analyse before molten steel solidification
Out, this heterogeneous nucleation point promotes the expansion of solidified structure proportion of equiaxed grain, so that the microscopic orientation of solidified structure disperses
Distribution advantageously reduces corrugation performance, but the addition of excessive titanium is easy to cause the blocking for smelting casting process, sets its content
No more than 0.5%.After the nitrogen-atoms in steel is completely fixed by titanium, Nb can be combined preferentially with carbon atom and be formed NbC, due to Nb's
Atomic radius is far longer than the atomic radius of Fe and Cr, and the NbC generated is also bigger to the effect of dragging of crystal boundary, can refine crystalline substance
Grain tissue, promotes the generation of texture orientation { 112 }<110>, to reduce production board corrugation height and surface roughness, while mistake
The Nb of amount will lead to Fe in steel2The formation of the hard phase of Nb deteriorates the formability of material, therefore the setting of its content is no more than 0.6%.Separately
Outside, in terms of the influence to ferrite stainless Steel Properties, the same niobium of zirconium, tantalum, titanium are similar, but tantalum is heavier than niobium, titanium, and zirconium,
Tantalum is very expensive, zirconium, tantalum can completely or partially substitute niobium and titanium, can choose niobium, titanium, zirconium, the addition of tantalum at least two obtain
Good anti-corrugation performance is obtained, needs to meet
Steel marcotexture of the present invention mainly passes through X-ray (X-ray diffraction method) and is measured, and then passes through measurement sample
{ 110 }, { 200 }, { 112 } three imperfect pole figures and orientation distribution function (ODF) is calculated, three-dimensional can determine by ODF figure
The intensity of each orientation in space, in the metal of BCC structure, it is only necessary to chooseSection, so that it may it is complete
Analysis Eulerian angles be (30 °, 55 °, 45 °) and (90 °, 55 °, 45 °) { 111 }<112>orientation intensity, the peak value of texture
Intensity is greater than 7.
It is obtained other than good deep drawability except through high { 111 } texture component intensity, the plane of thin plate is respectively to different
Property Δ r value and surface quality are also important index.The advantageous grain for improving ferritic stainless steel deep drawing quality is oriented to
{ 111 }-gamma fiber, such crystal grain orientation be ferrite crystal grain generated under the mode of texturing for bearing plane strain { 001 } <
011>, { 112 }<011>, { 111 }<011>-alpha fibers, formed further through Recovery and recrystallization.But ferritic stainless steel
Plate during the rolling process, mainly roll as caused by plane strain, when the deformation on surface layer mainly has hot rolling by the deformation of central core
Caused by the shear strain that very big frictional force generates between roller and steel band, both modes of texturing are simultaneous.And
The mode of texturing of shear strain is easy the orientation of crystal grain for { 110 }<001>-goss texture.Since { 111 } texture and Gauss knit
The orientation in atom solid matter face is different in structure, adds plate when bearing pressure deformation, the pressure that the shear strain layer on surface layer is born
Lower rate is higher than the reduction ratio that inner plane strained layer is born, and therefore, the elongation percentage that phase is rolled on the edge on surface layer is higher than internal elongation percentage,
In this way, the part of surface layer extensions more than inside can only ride out surface and form fold under the containing of interior metal.Therefore, iron element
The evolution mechanism of the surface wrinkling degree of body stainless steel and the deep-draw ability contained is identical, the raising of deep drawing quality and surface pleat
The aggravation of wrinkle is mutually adjoint.But to improve the forming property of ferritic stainless steel, it is desirable to inhibit corrugated generation,
Material deep drawability is improved simultaneously, needs to find equalization point therebetween.
Simultaneously as texture different in steel has different r values, the contribution to the r value of all directions is also different
, it is therefore desirable to microcosmic analysis is carried out, is mainly parsed using backscattered electron diffraction (EBSD), it is inclined by analytic angle
The content balance of different orientation of the difference within the scope of ± 20 °, the content of setting { 111 } component need to be greater than 55%.
The deep drawability of material is usually indicated with average plastic strain ratio (r), is processed into stretching examination according to JIS5 standard
Sample, measurement is parallel to the r value of rolling: r after stretching 15%0, the r value at 45 ° with rolling direction: r45, perpendicular to rolling direction
R value: r90.Its calculation formula is: average r=(r0+r90+2r45)/4.Steel of the invention is mainly high deep punching capability, therefore is set
Equal r value is allocated greater than 1.7.
Measure thin plate anisotropic index Δ r value, general calculation formula are as follows: Δ r=(r0+r90-2r45)/2,
Set its Δ r < 0.3.
The evaluation of corrugation height: select in parallel with the tensile sample of rolling direction, strain rate 10mm/min, pre-stretching
Stop stretching after 25%, then measures its wrinkle height Pt (wave crest and wave on perpendicular to rolling direction with surface roughometer
The difference in height of paddy), Pt value is at 25 μm or less.
The preparation method of low-cost high-strength austenitic stainless steel of the present invention, characterized in that include the following steps:
1) it smelts, forge
It smelted by above-mentioned chemical component, be forged into slab；
2) hot rolling
Heating temperature≤1200 DEG C, finishing temperature are 800~1000 DEG C；
3) hot-roll annealing
Hot-roll annealing temperature is 900~1050 DEG C, 5~6min of annealing time；
4) cold rolling
Cold rolling reduction ratio > 70%；
5) annealing after cold rolling
Annealing after cold rolling temperature is 850~1000 DEG C, 1~3min of annealing time, and controls average grain size at 20 μm
Below.
In design and manufacture technology of the invention:
Hot rolling heating and temperature control of the invention at 1200 DEG C hereinafter, finishing temperature is between 800~900 DEG C, finish to gauge temperature
The reduction of degree may advantageously facilitate the recrystallization of hot rolled plate, refinement crystal grain, be conducive to the performance improvement that wrinkles, but too low finish to gauge temperature
The increase of resistance of deformation when degree will lead to rolling, simultaneously because the shear-deformable difference with central core plane deformation in surface layer when rolling
Increase, leading to hot rolled plate microstructure, gradient is excessive in a thickness direction, leads to serious corrugation, therefore finishing temperature control
At 800 DEG C or more.
The stainless steel of all single ferritic structures of steel of the present invention completely can be long using high temperature in order to reduce energy consumption
The annealing of time, it is contemplated that hot-roll annealing has apparent hereditary effect to final production board, needs to realize the complete of hot rolled plate
Recrystallization.Therefore setting annealing temperature is at 900 DEG C or more, if temperature is lower than this temperature, non-uniform hot rolling banded structure meeting
It is genetic on production board through subsequent cold rolling, so as to cause the presence of apparent { 001 } crystal grain cluster, increases the ear height processed of production board
Degree and wrinkling.If 1050 DEG C of temperature, excessive grain is grown up, production board is difficult to realize increasing cold rolling reduction ratio
The refinement of crystal grain leads to the increase of surface roughness.This is also crucial control temperature of the invention.
The present invention sets cold rolling reduction ratio and is greater than 70%, to obtain low corrugation height, and realizes that finished product board group is knitted
Even property, it is necessary to need corresponding cold rolling reduction ratio, but excessively high reduction ratio will increase the load of milling train again, lead to production difficulty
Greatly.
Annealing after cold rolling is in the final stage of metallurgical technology process, and suitable temperature is needed to carry out final annealing.If
Annealing after cold rolling temperature is too low, it is difficult to obtain complete recrystallization, apparent mixed crystal easily occurs；Ferritic stainless steel is come
It says, annealing after cold rolling temperature is excessively high to also result in the excessively coarse of crystal grain, and grain-boundary weakness and surface roughness is caused to increase.Cause
This, annealing after cold rolling temperature selects between 850~1000 DEG C, and controls average grain size at 20 μm or less.
Beneficial effects of the present invention:
Emphasis of the present invention passes through hot rolling and cold rolled annealed by the compound additions of the stabilizing elements such as Nb, Ti, Ta, Zr
The optimization of system obtains good deep drawability and anti-corrugation performance.Since family's electrical article stainless steel is to deep drawing quality requirement
It is relatively high, based on the present invention, the high deep drawability of ferritic stainless steel can be efficiently used, low in-plane anisotropy and good
The good anti-corrugation performance of surface, meets actual application, and further expansion ferritic stainless steel is in electrical article industry
Application range.
Specific embodiment
Below with reference to embodiment, the present invention will be further described.
For steel embodiment ingredient of the present invention referring to table 1, table 2 is the manufacturing process of steel embodiment of the present invention.
By the ferritic stainless steel of ingredient melting shown in table 1 and it is forged into slab, then slab is heated, is passed through
The hot rolling for crossing 3-6 passage is made the hot rolled steel plate that plate thickness is 3mm-5mm and controls different finishing temperatures in this process；And
Afterwards by different hot-roll annealing technique, then annealed sheet is subjected to pickling to remove the iron scale on surface, by different cold
Final annealing, the product that manufacture is 0.35-2mm at plate thickness are carried out after rolling rolling schedule.Sample is intercepted on production board, is processed into
The tensile sample of JIS5 standard measures its r value on 0 °, 45 ° and 90 ° direction, calculates average r value and Δ r value.In addition, cutting
Marcotexture sample is taken, its orientation distribution function is measured, and calculates the peak value of { 111 }<112>orientation, is listed in Table 2 below；Most
Afterwards, crystal grain are orientated within the scope of ± 20 ° by owning { 111 } in production board after EBSD analysis heterogeneity, different manufacturing process
Gross area score, be listed in Table 2 below.
No. 1 steel is the steel for not adding any stabilizing element, and no matter hot rolled plate uses low temperature for a long time or high temperature, short time
Between anneal, all there is no good { 111 } component, content and intensity are all relatively low, and there is also obvious in its production board
Wrinkling, be unsatisfactory for the present invention, therefore using it as comparative example.
No. 2 steel are the ferritic stainless steel for adding titanium tantalum, and hot rolled plate uses different (900 DEG C -1050 of annealing temperature
DEG C) be heat-treated, the peak strength of { 111 }<112>is both greater than 7, and the area of { 111 } orientation in final production board
Score is also greater than 50%, and final average r value is 1.7 or more, but after the annealing temperature of hot rolled plate reaches 1050 DEG C, Δ
R value has been more than 0.3, and temperature is more than 1000 DEG C and is not belonging to the present invention, other belong to the present invention.
No. 3 steel are the ferritic stainless steel of niobium zirconium, and hot-roll annealing temperature is different: 920 DEG C and 960 DEG C, final
{ 111 } orientation content, the peak strength of { 111 }<112>orientation, r value and Δ r value all meet the present invention and impose a condition, because
This belongs to the present invention.
No. 4 steel ferritic stainless steel stable for Nb, Ti and Zr, either unannealed after hot rolling or low-temperature annealing,
Annealing temperature is below 900 DEG C, although unannealed production board obtains { 111 } component of high-content, anisotropy compared with
Greatly, wrinkling is serious, influences surface quality, and the low-temperature annealing of this hot rolled plate is easy to cause the banded structure heredity of hot rolled plate
Into production board, causes the aggregation of crystal grain cluster or ear height processed too big, be not belonging to the present invention.
Hot rolled plate is being higher than 900 DEG C of progress short time annealing, meets { 111 } component when temperature is lower than 1030 DEG C
Area ratio, and peak strength is very big, meet present invention provide that texture intensity and ratio；When temperature reaches 1030 DEG C, although
The increase of temperature promotes the dispersion of hot rolling banded structure, but the higher roughening for promoting hot rolled plate crystal grain of temperature, and not
Conducive to the raising of the abundant development and r value of final { 111 } component, it is consequently belonging to comparative example.
No. 5 steel are that the steel of Nb, Ti and Ta stable composition finds its { 111 } when carrying out 800 DEG C of low-temperature annealings to cold-reduced sheet
The content and low strength of texture, while having serious corrugation, it is unsatisfactory for the present invention；When annealing temperature gradually rises, 850
When DEG C -950 DEG C, the orientation intensity and content that the present invention limits, corrugation height and deep drawability all meet, and belong to this hair
It is bright；When temperature is further increased to 1050 DEG C, excessively growing up for crystal grain is degrading average r value, is not the present invention, belongs to ratio
Compared with example.
1 unit wt% of table
Table 2
Remarks: f (g)maxThe peak strength of { 111 }<112>component is represented in cold rolled annealed plate.
{ 111 } the area ratio refers to that deviation angle owns the gross area score of { 111 } orientation within the scope of ± 20 °.
Claims (8)
1. the ferritic stainless steel with favorable forming property, ingredient percent are as follows:
C:0.002%~0.02%,
N:0.002%~0.02%,
Si:0.05%~0.60%,
Mn:0.05%~0.50%,
Cr:15.0%~19.0%,
Ti:0~0.5%,
Nb:0~0.6%,
Zr:0~0.05%,
Ta:0~0.04%,
Surplus is Fe and inevitable impurity, and is met,
2. as described in claim 1 with the ferritic stainless steel of favorable forming property, characterized in that the depth of the stainless steel
Punching performance indicates that average r value is greater than 1.7, wherein r=(r with average plastic strain ratio r0+r90+2r45)/4, according to JIS5 standard
It is processed into tensile sample, measurement is parallel to the r value of rolling: r after stretching 15%0, the r value at 45 ° with rolling direction: r45, hang down
Directly in the r value of rolling direction: r90；The evaluation of corrugation height: corrugation height Pt, the difference in height of wave crest and trough, Pt value is less than 25 μ
m。
3. as claimed in claim 1 or 2 with the ferritic stainless steel of favorable forming property, characterized in that the ferrite
The marcotexture of stainless steel, in the metal of body-centered cube BCC structure, Eulerian angles be (30 °, 55 °, 45 °) and (90 °, 55 °,
45 °) { 111 }<112>orientation intensity, the peak strength of texture is greater than 7.
4. the ferritic stainless steel with favorable forming property as described in claims 1 or 2 or 3, characterized in that the iron element
Body stainless steel in-plane anisotropy Δ r value, its calculation formula is: Δ r=(r0+r90-2r45)/2 set its Δ r < 0.3.
5. the ferritic stainless steel with favorable forming property as claimed in claim 1 or 2 or 3 or 4, characterized in that described
The cold rolling finished product of ferritic stainless steel, the content of { 111 } orientation crystal grain is more than 55% in ± 20 ° of deviation ranges.
6. the ferritic stainless steel with favorable forming property as described in claims 1 or 2 or 3 or 4 or 5, characterized in that institute
The average grain size of ferritic stainless steel is stated at 20 μm or less.
7. the preparation method of the ferritic stainless steel with favorable forming property as described in claim 1~6 any one,
It is characterized in, includes the following steps:
1) it smelts, forge
It smelted by chemical component described in claim 1, be forged into slab；
2) hot rolling
Heating temperature≤1200 DEG C, finishing temperature are 800~1000 DEG C；
3) hot-roll annealing
Hot-roll annealing temperature is 900~1050 DEG C, 5~6min of annealing time；
4) cold rolling
Cold rolling reduction ratio > 70%；
5) annealing after cold rolling
Annealing after cold rolling temperature is 850~1000 DEG C, 1~3min of annealing time.
8. the preparation method of the ferritic stainless steel with favorable forming property as claimed in claim 7, characterized in that described
The average grain size of ferritic stainless steel is at 20 μm or less.
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| WO2023075283A1 (en) * | 2021-10-25 | 2023-05-04 | 주식회사 포스코 | Ferritic stainless steel with excellent clad sheet workability, and manufacturing method therefor |
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