CN105624559A - Thick-gauge ultra-deep drawing cold rolled steel plate and manufacturing method thereof - Google Patents
Thick-gauge ultra-deep drawing cold rolled steel plate and manufacturing method thereof Download PDFInfo
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Abstract
The present invention relates to a thick-gauge ultra-deep drawing cold rolled steel plate and a manufacturing method thereof. In the prior art, when the cold rolling reduction rate is insufficient, the stamping performance of the ultra-deep drawing cold rolled steel plate with the thickness of 1.2-2.0 mm and produced by using the bell furnace annealing process does not meet the standard. A purpose of the present invention is to solve the technical problem in the prior art. The chemical components of the thick-gauge ultra-deep drawing cold rolled steel plate comprise, by weight, less than or equal to 0.003% of C, less than or equal to 0.03% of Si, 0.1-1.0% of Mn, less than or equal to 0.02% of P, less than or equal to 0.02% of S, less than or equal to 0.005% of N, less than or equal to 0.05% of Alt, and the balance of Fe and unavoidable impurities, wherein the content of Ti% satisfies the equation that (Ti%)-3.4*(N%)-1.5*(S%)-4*(C%) is (0.004-0.03). According to the present invention, the thick-gauge ultra-deep drawing cold rolled steel plate is mainly used for outer covers, shells and other members of mechanical and electrical products.
Description
Technical field
The present invention relates to a kind of ultra-deep punching cold-rolling steel sheet, particularly to a kind of think gauge ultra-deep punching cold-rolling steel sheet and manufacture method thereof.
Background technology
Thickness is outer housing and the housing that the think gauge cold-reduced sheet of 1.2-2.0mm is mainly used in electronic product; as structural member; owing to having good rigidity; the apparatus run under certain working condition, precision optical machinery etc. can be played a protective role, and reach the effect of damping noise reduction to a certain extent. Along with the volume miniaturization of machinery etc., purposes variation, the profile of outer housing and housing also becomes increasingly complex, and the requirement of material is also improved constantly by its punch forming process.
Ultra-low carbon gapless atomic steel (IF steel), due to containing carbonitride-forming elements, it is possible to reduce steel grade solid solution carbon and nitrogen atoms content greatly, thus obtaining excellent processability in cold-rolled products. So that the deep drawability of cold-rolled products and other many-sided performance reach optimization, according to manufacturing different-alloy system that IF steel adopts, intensity rank, cold rolling number of times, different annealing way, annealing times etc., have been carried out substantial amounts of composition and technique is groped.
Such as, China Patent Publication No. CN102884213A discloses the excellent cold-rolled steel sheet of the shape uniformity after a kind of and outside plate etc. for automobile, soft and processing and manufacture method thereof. Each surface on its steel plate two surface is smaller in size than the content (quality %) of the Ti element contained in the precipitate of 20nm in the thickness of slab skin section to 10 ��m be less than the 9% of Ti content (quality %) total in steel plate. Its cold rolling reduction ratio is 50-90%, it is preferable that more than 70%.
China Patent Publication No. CN101880827B discloses automobile IF steel and the production method of a kind of �� r��0.3. Its chemical constituent and percentage by weight: C:0.0009��0.0049, Si :��0.015, Mn:0.07��0.21, P :��0.025, Nb:0.015��0.049, Ti:0.01��0.06, Als:0.015��0.07, S:< 0.015, N:< 0.005. It contains Nb element, and cold rolling reduction ratio is 67-80%; Adopting continuous annealing mode, think gauge product is significantly high to even moving back capacity of equipment requirement.
China Patent Publication No. CN101135025A discloses a kind of bell furnace and produces cold rolling high-strength ultra-deep-drawing steel plate and manufacture method thereof. C��0.006, Si��O.30, Mn:0.15-1.40, P��0.08, S��0.02, N:0.001-0005, Al:0.03-0.06, its addition of B:0.0003-0.002, Ti and Nb respectively Ti-(48/14) N=(0.005-0.015), Nb-(93/12) C=(0-0.03). Its cold rolling reduction ratio is more than 73%.
Restriction due to the common cold rolling continuous rolling plant ability of current most domestic, in the ultra-deep of 1.2-2.0mm, cold-rolled products are rushed for thickness and is not provided that enough cold rolling reduction ratios, particularly the deformation extent of think gauge product core is relatively smaller, thus postponing recrystallization process and affecting processability. Although China Patent Publication No. CN101880827B discloses the IF product made from steel that can produce relatively think gauge, but containing Nb in its component system, and the production of high-temperature, think gauge, continuous annealing apparatus Capability Requirement is high.
Prior art lacks when cold rolling reduction ratio deficiency, adopt batch annealing to produce the method that the good 1.2-2.0mm thickness ultra-deep of punching performance rushes cold-rolled products.
Summary of the invention
In order to overcome the deficiencies in the prior art, needing to provide a kind of think gauge ultra-deep punching cold-rolling steel sheet and manufacture method thereof, the present invention passes through to adopt suitable composition design, hot rolling, cold rolling and annealing process design, with conventional cold rolling continuous rolling plant, it is manufactured that the ultra-deep punching cold-rolling steel sheet of think gauge.
It is an object of the invention to provide a kind of think gauge ultra-deep punching cold-rolling steel sheet and manufacture method thereof, the technical problem that the punching performance of the thickness 1.2-2.0mm ultra-deep punching cold-rolling steel sheet produced when solving existing cold rolling reduction ratio deficiency is not up to standard with batch annealing.
Applicant is through experimental study for many years, it has been found that adopt conventional IF steel production technology, through bell-type annealing, although think gauge IF product made from steel recrystallization is abundant, and yield strength is at below 150MPa, and thin slab product is suitable; But, its plastic strain ratio weighted meanValue is only about 1.5, comparatively speaking, the thickness IF steel less than 1.0mm, its plastic strain ratio weighted meanValue is about 2.0.
During cold rolling reduction ratio deficiency, the favorable texture formed in cold-rolled process is relatively weak; And owing to the deformation energy of accumulation is less, the inhibition of steel grade second phase particles, the temperature of bell-type annealing is more much lower than the temperature of continuous annealing in addition, thus driving force is substantially little, production process is slow, can not preferential growth in recrystallization process, it is impossible to obtain favourable { 111} texture. Therefore, for the think gauge IF steel cold-rolled products that bell-type annealing produces, affect the factor of its mouldability according to importance sorting, be followed successively by: coiling temperature, heating cycle, hot rolled plate texture.
IF steel is extremely low due to interstitial atom content, deformation process is passed through dislocation motion, born of the same parents' shape substructure easily occurs, cumulative thus with cold roller and deformed rate, deformation process is formed { 111} texture becomes strong, and carbon aluminium-killed steel, grain orientation can be occurred when reduction ratio is higher to rotate, form non-favorable texture, therefore, after recrystallization completes, the processability of IF steel is better than carbon aluminium-killed steel. But, when IF steel deformation rate is relatively low, or when recrystallization process meets with obstruction, especially with the bell-type annealing mode that temperature is relatively low, the forming core of crystal grain and grow up and can be affected, show as favorable texture in recrystallization process to be not easy in short period development fully, and after recrystallization, unfavorable texture is easily formed, thus reducing the processability of material.
Recrystallization process is formed inhibition, mainly the second phase particles in steel. However, to ensure that finish rolling carries out in the austenitic temperature interval of steel, the heating-up temperature of continuous casting billet inevitably reaches more than 1100 DEG C. This temperature range long-time heat preservation, can make Ti4S2C2A large amount of dissolvings. In subsequent hot rolled process, the Ti of precipitation4S2C2Particle size is substantially little with comparing in original strand, and precipitates out the TiC particle of a lot of disperse simultaneously. Second phase particles is more little, and the effect that recrystallization is hindered is more obvious.
If the second phase particles containing Ti precipitates out undersized, cold rolling total deformation is not enough, then cold rolling favorable texture is not enough to overcome the obstruction of little particle to be preferentially developed in recrystallization process. And at high temperature in long term annealing process, along with the ripening of fine second phase particles, recrystallization process slowly carries out, thus the crystal grain of different texture can be grown up at same time period forming core, is unfavorable for obtaining { 111} texture. And be incubated at relatively high temperatures after hot rolling, it is possible to it is obviously improved size and the distribution situation of second phase particles. Having investigated the impact on final cold-reduced sheet processability of the hot-rolled sheet coil heat insulation effect, be found by experiment that, when coiling temperature is less than 700 DEG C, think gauge cold-reduced sheet can not meet the purposes of ultra-deep punching.
Additionally, cold rolling texture is had obvious hereditation by hot rolling texture, especially when cold rolling total deformation is not enough, hot rolled plate texture seems extremely important. Thicker roughed bloom, it is possible to obtain bigger drafts, obtains more tiny crystal grain after finish rolling, favourable for processability; Simultaneously slightly above implementing cooling in the Ar3 temperature short time after finish rolling terminates, a large amount of deformation energy is accumulated again owing to austenite stacking fault energy is higher, thus save stronger non-recrystallization zone rolling texture, { 112}, { 113}, { 332} hot rolled plate texture, and quickly cool down and weaken disadvantageous { 001}<110>phase transformation texture further advantageously can be formed. Certainly, according to its importance degree to think gauge IF steel processability, improving Phase cooling speed should to ensure premised on coiling temperature.
Applicant is through experimental study, it has been found that need the original texture of second phase particles size and the distribution, hot rolled plate strictly controlling in IF steel in the hot rolling, with this manufacture at the cold rolling ultra-deep punching cold-rolling steel sheet realizing think gauge.
The technical solution used in the present invention is:
A kind of think gauge ultra-deep punching cold-rolling steel sheet, its chemical component weight percentage ratio is: C��0.003%, Si��0.03%, Mn:0.1%��1.0%, P��0.02%, S��0.02%, N��0.005%, Alt��0.05%, Ti%:(Ti%)-3.4 �� (N%)-1.5 �� (S%)-4 �� (C%)=(0.004 ~ 0.03), surplus is Fe and inevitable tramp element.
The reason that the chemical composition of think gauge ultra-deep punching cold-rolling steel sheet of the present invention is limited in above-mentioned scope is as follows:
Carbon: carbon is solution strengthening element, is favorably improved intensity, and the raising of rigidity is favourable, but in order to obtain excellent deep drawing quality, should reduce as far as possible. Additionally, when containing carbon in a large number, in steel, the carbide amount of titaniferous increases, and is unfavorable for follow-up recrystallization. Carbon content��0.003% that the present invention sets.
Silicon: silicon is solid-solubilized in steel matrix to have significantly strengthens effect, but silicone content is too high unfavorable to steel plate plasticity and toughness, and the too high meeting of silicone content simultaneously forms the serious Fe being difficult to remove on hot rolled plate surface2O3, affecting product appearance and sequent surface processes, the present invention limits silicone content��0.03%.
Manganese: manganese makes hardness of steel increase as solution strengthening element. In order to ensure steel plate rigidity, it is necessary to containing the manganese of more than 0.1%. But excessive containing can hinder processability. The present invention limits Mn content as 0.1%��1.0%.
Phosphorus: phosphorus is solution strengthening element, the strengthening of steel and the raising of yield strength is effective. But, phosphorus content is higher can cause fire check, cold crack constantly, and the present invention limits P��0.02%.
Sulfur: the easy segregation of sulfur, and plate quality harm is relatively larger, and sulfur should control at reduced levels as far as possible. Ensure certain molding and deep drawability, it is desirable to reducing the sulfur content in steel, the present invention limits S��0.02% as far as possible.
Nitrogen: titanium nitride and titanium carbide coherence, it is possible to reduce the quantity of the titanium carbide particle that disperse is fine, is also a kind of inevitably impurity element simultaneously. But it is favourable to processability to reduce nitrogen content, and the addition of titanium alloy can be reduced, therefore more few more good. The present invention limits N��0.005%.
Aluminum: aluminum is the element contained as deoxidizer, it is possible to ensureing deoxidation effect, the present invention limits Alt content��0.05%.
Titanium: titanium is for fixing carbon in steel, nitrogen, sulfur, it is necessary to the ratio of its excess-three kind Elements Atom amount determined required minimum Ti content according to it. Steel exists a certain amount of residual titanium (being set greater than 0.004% in the present invention), except reduce further the carbon of free state, number of nitrogen atoms so that it is guaranteed that steel plate without timeliness except, simultaneously to improve steel plate Lankford r value favourable. But excessive residual titanium can improve the temperature of recrystallization. Thus the present invention sets residual titanium content as 0.004% ~ 0.03%, Ti content is (Ti%)-3.4 �� (N%)-1.5 �� (S%)-4 �� (C%)=(0.004 ~ 0.03).
A kind of manufacture method of think gauge ultra-deep punching cold-rolling steel sheet, the method includes:
Molten steel carries out continuous casting after Fruit storage and obtains continuous casting steel billet, the mass percent of wherein said molten steel composition is: C��0.003%, Si��0.03%, Mn:0.1%��1.0%, P��0.02%, S��0.02%, N��0.005%, Alt��0.05%, Ti%:(Ti%)-3.4 �� (N%)-1.5 �� (S%)-4 �� (C%)=(0.004 ~ 0.03), surplus is ferrum and is unavoidably mingled with.
Continuous casting steel billet is in 1100 DEG C��1200 DEG C, hot rolling is carried out after heating 150��240min, described hot rolling is two-part rolling mill practice, roughing is 5 passage tandem rollings, roll more than austenite recrystallization temperature, roughing end temp is 1030 DEG C��1070 DEG C, workpiece thickness >=39mm after breaking down, finish rolling is 7 passage tandem rollings, and in austenite non-recrystallization temperature interval rolling, finish rolling end temp is 900 DEG C��940 DEG C, after finish rolling, steel plate thickness is 3mm��5mm, and section cooling adopts leading portion cold by force, and coiling temperature is 710 DEG C��760 DEG C and batches to obtain coils of hot-rolled steel;
By above-mentioned coils of hot-rolled steel again uncoiling, after pickling, reversable mill or 5 Stands Cold Tandem Mills carry out cold rolling, cold rolling reduction ratio is 60%��73%, steel band after cold roller and deformed through bell-type annealing furnace annealing, smooth, batch and obtain the finished steel plate that thickness is 1.2mm��2.0mm, described annealing region is 720 DEG C��750 DEG C, and the annealing soak time is 3h��30h, and smooth elongation percentage is 0.5%��2.0%.
The manufacturing process system reason that the present invention takes is as follows:
1, the setting of continuous casting steel billet heating-up temperature and heat time heating time
Continuous casting steel billet heating-up temperature is too low, and rolling temperature reduces and is difficult to make hot rolling carry out between austenitic area, it is impossible to ensure finishing temperature. By calculation of thermodynamics, heating-up temperature is more than 1200 DEG C, and comparatively thick (Ti, Mn) the S second phase particles generated in casting process can dissolve in a large number, and generates the nano-precipitations of disperses in ensuing operation in a large number. In the temperature range set, if heat time heating time is too short, continuous casting billet cannot be completely heated up, if carrying out long-time heating, can cause the Ti in strand4S2C2Particle (its solution temperature is relatively low) dissolves in a large number, and generates tiny Ti in the hot rolling4S2C2Particle. Therefore the present invention sets continuous casting steel billet heating-up temperature as 1100 DEG C��1200 DEG C, and heat time heating time is 150min��240min.
2, the setting of hot rolling roughing end temp and workpiece thickness
Hot rolling roughing makes the Austenite Grain Refinement in strand, it is ensured that obtain good structural state through ferrite transformation after hot fine rolling. Workpiece thickness affects steel plate finishing temperature, particularly steel plate edge finishing temperature, if intermediate blank temperature drop is excessive, follow-up finish rolling finishing temperature can be affected, particularly steel plate edge temperature drop is very big, and steel plate edge is in two-phase section rolling, causes the sharply deterioration of forming property. Additionally, thicker intermediate blank is conducive in the finish rolling stage, accumulative more deformation energy, thus obtaining tiny crystal grain, it is thus achieved that relatively favourable hot rolling texture. The present invention sets hot rolling roughing and rolls more than recrystallization temperature, and hot rolling roughing finishing temperature is 1030 DEG C��1070 DEG C, workpiece thickness >=39mm.
3, the setting of hot fine rolling end temp and cooling system
Hot fine rolling end temp is too high, is unfavorable for forming stronger rolling texture, also hinders hot rolled plate to form relatively favourable texture. Steel billet temperature when hot fine rolling terminates is lower than Ar3During transformation temperature, i.e. finish rolling part occurs at two-phase section, thus damaging uniformity, plate property is unfavorable. In addition, after finish rolling terminates, if steel plate rate of cooling is relatively slow, ferrite transformation is slower development also, ferrite crystal grain is relatively coarse, it is unfavorable for being saved in the favourable rolling texture that non-recrystallization zone obtains, also being unfavorable for reducing unfavorable phase transformation texture, the final hot rolled plate texture obtained is also quite unfavorable, causes that the plastic strain ratio degree of anisotropy �� r value of final think gauge cold-rolled products worsens. The present invention sets hot fine rolling finishing temperature as 900 DEG C��940 DEG C, and finish rolling terminates section cooling and adopts leading portion cold by force.
4, hot-rolling coiling temperature sets
Higher coiling temperature and Slow cooling condition, be primarily to sufficient power and the time of providing to the maturing process of the second phase particles in IF steel, reduce the performance inconsistency of inner ring of steel coil and outer ring simultaneously. As it was previously stated, be found by experiment that, when coiling temperature is less than 700 DEG C, think gauge cold-reduced sheet can not meet the purposes of ultra-deep punching. Additionally, as too fast in cooling, coiled sheet Internal and external cycle has obvious thermograde, and faster, its punching performance is relatively poor for outer ring temperature drop, and the present invention sets hot-rolling coiling temperature as 710 DEG C��760 DEG C, Slow cooling after hot rolled steel plate rolling.
5, cold rolling reduction ratio sets
In order to realize the production of the think gauge ultra-deep punching cold-rolling steel sheet of IF steel on conventional cold rolling continuous rolling plant, the rolling power according to conventional cold rolling continuous rolling plant, the present invention sets cold rolling reduction ratio as 60%��73%.
6, annealing temperature and annealing time set
The present invention adopts existing bell-type to move back stove and is annealed processing. In order to make the IF steel plate of think gauge obtain sufficient recrystallization power, annealing temperature should be high as far as possible. Being subject to bell-type and move back the restriction of furnace apparatus ability, annealing temperature is not generally possible to reach Ac3Temperature spot, generates unfavorable texture without generating portion austenite phase transformation. Additionally, should according to the specification of cold-rolled steel sheet, volume weight, the annealing temperature of reasonable set bell-type annealing and annealing time. Considering, the present invention sets annealing temperature as 720 DEG C��750 DEG C; Annealing time is set as 3h��30h.
The thickness that the present invention obtains is the microscopic structure of the ultra-deep punching cold-rolling steel sheet of 1.2mm��2.0mm is ferrite, tissue grain size number is I 6.5��7.5 grades, the tensile strength Rm of steel plate >=300MPa, yield strength Rp0.2 are 140MPa��170MPa, elongation after fracture A80>=40%, plastic strain ratio weighted mean>=1.8, absolute value | the �� r |��0.4 of plastic strain ratio degree of anisotropy �� r value.
The present invention has following good effect compared to existing technology:
The present invention is by adopting the composition designs such as optimized alloy titanium and the hot rolling improved, cold-rolling process design, obtain the ultra-deep punching cold-rolling steel sheet that thickness is 1.2mm��2.0mm, adopting conventional cold continuous rolling milling train and bell-type to move back stove, the material produced has possessed good punching performance.
Accompanying drawing explanation
Accompanying drawing 1 is the cold-rolled steel sheet metallographic structure photo of the embodiment of the present invention 2.
Detailed description of the invention
Disclosed in disclosed in embodiment 1��6 and comparative example 1 China Patent Publication No. CN102884213A, comparative example 2 China Patent Publication No. CN101135025A, the present invention will be further described, as shown in table 1 ~ table 4.
Table 1 chemical composition of the present invention (percentage by weight %), surplus is Fe and inevitable impurity.
According to the requirement of material composition of the present invention design, adopt molten iron pre-desulfurization, converter top bottom blowing; blowing Ar station bottom blowing Ar and ensure stirring, RH stove vacuum circulation degassing processes, it is ensured that the pure degassing time of RH was more than 10 minutes; whole process blows Ar protective casting, cuts into scale continuous casting steel billet after casting.
After the heated stove of continuous casting steel billet reheats, Continuous Heat tandem rolling mill rolls, process control parameter is in Table 2, after roughing milling train and finish rolling Continuous mill train controlled rolling, through section cooling, section cooling adopts leading portion cold by force, then batches, batch rear coiled sheet Slow cooling, produce qualified hot-rolled sheet coil.
Table 2 hot rolling technology of the present invention controls parameter
By above-mentioned coils of hot-rolled steel again uncoiling after overpickling, reversable mill or 5 Stands Cold Tandem Mills carry out cold rolling, according to final product thickness, it is 60%��73% that cold rolling reduction ratio controls, the steel band after cold roller and deformed through bell type annealing furnace, smooth, batch the finished steel plate obtaining thickness 1.2mm��2.0mm. Annealing process is: steel band is 720 DEG C��750 DEG C in bell type annealing furnace annealing region, and the annealing soak time is 3h��30h. Cold rolling and annealing process controls parameter in Table 3.
Table 3 present invention is cold rolling, anneal, flattening process controls parameter
Utilize the ultra-deep punching cold-rolling steel sheet that the thickness that said method obtains is 1.2mm��2.0mm, with reference to accompanying drawing, the microscopic structure of cold-rolled steel sheet is ferrite, and according to " GB/T6394-2002 metal mean grain size algoscopy ", measuring its tissue grain size number is I 6.5��7.5 grades.
The ultra-deep punching cold-rolling steel sheet that the thickness present invention obtained is 1.2mm��2.0mm carries out tension test according to " GB/T228.1-2010 metal material stretching test part 1: room temperature test method ", mechanics properties testing is carried out according to " mensuration of GB/T5027-2007 metal sheet and strip plastic strain ratio (r value) ", mechanical performance data is in Table 4, and in table 4, the testing standard of the elongation after fracture of listed comparative example 1 is JISZ2241.
The tensile strength Rm of the steel plate of the cold-rolled steel sheet that the present invention obtains >=300MPa, yield strength Rp0.2 are 140MPa��170MPa, elongation after fracture A80>=40%, plastic strain ratio weighted mean>=1.8, absolute value | the �� r |��0.4 of plastic strain ratio degree of anisotropy �� r value.
The mechanical property of table 4 cold-rolled steel sheet of the present invention
The cold-rolled steel sheet product that the present invention obtains has good punching performance.
In addition to the implementation, the present invention can also have other embodiments. All employings are equal to replacement or the technical scheme of equivalent transformation formation, all fall within the protection domain of application claims.
Claims (6)
1. a think gauge ultra-deep punching cold-rolling steel sheet, its chemical component weight percentage ratio is: C��0.003%, Si��0.03%, Mn:0.1%��1.0%, P��0.02%, S��0.02%, N��0.005%, Alt��0.05%, Ti%:(Ti%)-3.4 �� (N%)-1.5 �� (S%)-4 �� (C%)=(0.004 ~ 0.03), surplus is ferrum and is unavoidably mingled with.
2. think gauge ultra-deep punching cold-rolling steel sheet as claimed in claim 1, its microscopic structure is ferrite, and tissue grain size number is I 6.5��7.5 grades.
3. think gauge ultra-deep punching cold-rolling steel sheet as claimed in claim 1 or 2, the yield strength Rp0.2 of its 1.2mm��2.0mm thick cold rolled steel sheet is 140MPa��170MPa, tensile strength Rm >=300MPa, elongation after fracture A80>=40%, plastic strain ratio weighted mean>=1.8, absolute value | the �� r |��0.4 of plastic strain ratio degree of anisotropy �� r value.
4. the manufacture method of the think gauge ultra-deep punching cold-rolling steel sheet as described in as arbitrary in claim 13, including:
Molten steel carries out continuous casting after Fruit storage and obtains continuous casting steel billet;
Continuous casting steel billet is in 1100 DEG C��1200 DEG C, carrying out hot rolling after heating 150��240min, described hot rolling is two-part rolling mill practice, and roughing is 5 passage tandem rollings, roll more than austenite recrystallization temperature, roughing end temp is 1030 DEG C��1070 DEG C, and finish rolling is 7 passage tandem rollings, in austenite non-recrystallization temperature interval rolling, finish rolling end temp is 900 DEG C��940 DEG C, after finish rolling, section cooling adopts leading portion cold by force, and coiling temperature is 710 DEG C��760 DEG C and batches to obtain coils of hot-rolled steel;
Coils of hot-rolled steel is uncoiling again, through pickling, cold rolling, bell-type annealing furnace annealing, smooth, batch that to obtain thickness be 1.2mm��2.0mm finished steel plate, described cold rolling reduction ratio is 60%��73%, annealing temperature is 720 DEG C��750 DEG C, annealing time is 3h��30h, and smooth elongation percentage is 0.5%��2.0%.
5. the manufacture method of think gauge ultra-deep punching cold-rolling steel sheet as claimed in claim 4, it is characterised in that workpiece thickness >=39mm after breaking down.
6. the manufacture method of think gauge ultra-deep punching cold-rolling steel sheet as claimed in claim 4, it is characterised in that after finish rolling, hot rolled steel plate thickness is 3mm��5mm.
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