CN104233062A - Extra-deep drawing hot-galvanized steel plate produced by annealing in short time and production method thereof - Google Patents
Extra-deep drawing hot-galvanized steel plate produced by annealing in short time and production method thereof Download PDFInfo
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Abstract
The invention relates to an extra-deep drawing hot-galvanized steel plate produced by annealing in short time and a production method thereof, and belongs to the technical field of iron-based alloys. The production method solves the problem that the existing horizontal furnace annealing production method of an extra-deep drawing hot-galvanized steel plate has short annealing time and produces products having extra-deep drawing performances lower than requirement standards. The extra-deep drawing hot-galvanized steel plate comprises 0.0009-0.0018% of C, less than or equal to 0.03% of Si, 0.08-0.13% of Mn, 0.030-0.062% of Ti, less than or equal to 0.0018-0.0036% of N, less than or equal to 0.004-0.008% of S and the balance Fe and unavoidable impurity elements, wherein a ratio of Ti/(4C+3.4N+1.5S) is 1.3-2.0 and a ratio of Mn/S is 10-30. The extra-deep drawing hot-galvanized steel plate has a steel plate microstructure grain size level of I6.0-I7.0, yield strength of 130-165MPa, tensile strength of 280-310MPa and percentage elongation A80mm after fracture of 40-49%, is suitable for preparation of household electrical appliance and hardware parts having extra-deep punching forming processing requirements and has low material yield strength and high molding reliability.
Description
Technical field
The present invention relates to a kind of short period of time annealing production ultra-deep and rush hot-dip galvanizing sheet steel and production method thereof, its steel plate microstructure grain size number is I6.0 ~ I7.5 level, yield strength is 130 ~ 165MPa, tensile strength is 280 ~ 310MPa, elongation after fracture A80mm is 40% ~ 49%, be applicable to household appliances, five metals has ultra-deep punching forming processing request parts, material yield strength is low, and shaping reliability is high.
Background technology
Along with domestic household electrical appliances, the continuing to optimize of hardware industry product structure design, increasing spare and accessory parts show as complex structure, shaping difficulty is large, the raising of forming requirements simultaneously also proposes more and more higher requirement to starting material, in household appliances purposes, pot galvanize end-use is the widest, because its zinc layers material ductility is good, pot galvanize product has extraordinary processability, the product of pot galvanize simultaneously has very good corrosion resisting property and lower cost, and deep draw galvanizing production is used widely in household electric appliances.
Its raw material of deep-draw cold rolling hot dip galvanizing product adopts equal IF component system to design, and usual IF steel is divided into Ti-IF, Nb-Ti-IF and Nb-IF steel, and wherein Ti-IF cost is minimum, and its recrystallization annealing temperature is also minimum, is that deep drawing steel product design is first-selected.Deep-draw cold rolling hot dip galvanizing product is direct hot dip after continuous annealing process; in existing production technology, continuous annealing furnace is divided into vertical heater and horizontal chamber oven; its essential difference is that annealing temperature and annealing time differ greatly; because of vertical heater annealing segment length; long period annealing time can be realized; be easy to get the galvanizing production of deep drawability; usual annealing time is not as technical protection point; but deep drawing steel data is produced seldom for the annealing of horizontal chamber oven short period of time, especially the open solution of production extra-deep drawing steel is not also had.
Chinese patent: 200710048926.8, the production method of deep drawing skin-passed hot-dip galvanizing sheet steel, disclose the production method of deep drawing skin-passed hot-dip galvanizing sheet steel, its carbon content scope 0.0030-0.0060%, Ti-3.4N-4C-1.5S content range 0.02-0.04%, roll and be chilled to 700-780 DEG C soon afterwards, anneal in 780 ~ 880 DEG C of temperature ranges, obtain product yield strength 185-190MPa, tensile strength 310-320MPa, elongation A8041-43%, finished product grain fineness number is 10.5 grades, this patent effect does not reach the object of the invention, its process implementing temperature range is larger, implementation result is bad to be determined.
Chinese patent: 201210141737.6, a kind of Nb, Ti compound ultra-deep punching galvanized sheet and production method, C≤0.0022%; Si≤0.006%; Mn0.08 ~ 0.16%; P≤0.009%; S≤0.008%; Ti0.033 ~ 0.04%; Nb0.012 ~ 0.017%; Als, 0.025 ~ 0.045%; N≤28ppm, surplus is Fe; Annealing temperature 850-860 DEG C, annealing time 200-600 second, the finished product yield strength≤155MPa, tensile strength is 260 ~ 330MPa, unit elongation >=44%, this patent effect can reach the requirement of ultra-deep punching performance, its shortcoming is that cost is higher for Nb-Ti-IF designs, and adding of Nb causes anneal of material difficulty to strengthen, annealing time reaches 200-600 second, and this technology cannot be implemented in the inventive method.
Chinese patent: 96190409.7, there is the ultralow carbon cold-rolled steel plate and steel plate galvanized and production technique thereof that improve fatigue property, steel plate contains weight percent: 0.0001-0.0026%C, maximum 1.2%Si, 0.03-0.3%Mn, 0.015-0.15%P, 0.0010-0.020%S, 0.005-0.1%Al, 0.0005-0.008%N, 0.0003-0.0030%B, all the other are Fe and inevitable impurity, its processing method rolls in rear 1.5S, with the speed of cooling of 50 DEG C/sec, hot rolled strip is cooled to 750 DEG C, and cold-rolled steel strip carries out continuous annealing at 600-900 DEG C.This patent does not reach require problem to solve existing IF product made from steel Welding Area fatigue property, and its chemical composition is Ultra-low carbon aluminium killed steel, surrenders 157-227MPa in embodiment, does not reach the object of the invention.Its technique to be coiling temperature be room temperature is to 750 DEG C, and annealing temperature is 600-900 DEG C, and scope is big, and reasonable implementation cannot be selected interval and ensure implementation result.
Summary of the invention
The object of this invention is to provide a kind of short period of time annealing production ultra-deep and rush hot-dip galvanizing sheet steel and production method thereof, mainly solve in prior art and adopt horizontal chamber oven annealing production ultra-deep to rush hot-dip galvanizing sheet steel, because annealing time is short, product ultra-deep punching performance does not reach the technical problem of requirement.
The present invention studies through long-term experiment, finds the relation of product composition, process and performance, solves the production technology difficult problem that short period of time ultra-deep rushes hot dip.Technical thought is: design is suitable for the component system of short period of time annealing, by the interpolation of low-carbon (LC), low manganese and suitable titanium elements, reach the object of fixing steel carbon, nitrogen, sulphur, reduce the solid solution strengthening effect of carbon, manganese element, thick carbon nitrogen sulphur titanium compound can be separated out again simultaneously and reduce annealing recrystallization temperature, short period of time completes material re-crystallizes and anneals and control grain growth, reaches product low surrender ultra-deep strategically important place and asks.
For achieving the above object, the chemical composition (weight percent) of substrate of the present invention is: C:0.0009% ~ 0.0018%, Si :≤0.03%, Mn:0.08% ~ 0.13%, Ti:0.030% ~ 0.062%, N≤0.0018 ~ 0.0036%, S≤0.004 ~ 0.008%, surplus is Fe and inevitable tramp element.Wherein Ti/ (4C+3.4N+1.5S) ratio 1.3-2.0, Mn/S ratio 10-30.
It is as follows that short period of time of the present invention annealing production ultra-deep rushes the reason that hot-dip galvanizing sheet steel chemical composition is limited in above-mentioned scope:
Carbon: in product of the present invention, wish that carbon content is more low better, because carbon solid solution in steel plays strengthening effect to matrix, simultaneously the carbide that formed of carbon and titanium also can some strengthening effect, by studying the impact of different carbon content on product yield strength, when carbon content is more than 0.0020%, material yield strength significantly improves, and too low carbon content production difficulty is larger, therefore, technical solution of the present invention setting C content scope is 0.0009% ~ 0.0018%.
Nitrogen: rush nitrogen and carbon in cold rolling hot dip galvanizing steel plate in ultra-deep and play strengthening to matrix equally, unfavorable to steel plate deep drawability, wish that nitrogen content is more low better, the same production difficulty of too low nitrogen content is large.Technical solution of the present invention setting N content 0.0018 ~ 0.0036%.
Titanium: adding by Ti, combines with C, N, S atom further, generates the carbon nitrogen sulfur compound of Ti, thus eliminate free C, atom N, realizes gapless solid solution atom in steel and exists.The content of titanium and carbon, nitrogen, sulphur content are relevant, when finding that Ti/ (4C+3.4N+1.5S) ratio is too low by research, steel can not fixedly cause the strength of materials to improve because still having carbon, nitrogen-atoms very well, because the raising of material re-crystallizes temperature causing annealing, because the time, not reaching ultra-deep rushes low surrender effect not when the ratio is too high simultaneously, therefore, technical solution of the present invention setting Ti content is 0.030% ~ 0.062%, and this inventive features is control Ti/ (4C+3.4N+1.5S) ratio is 1.3-2.0.
Manganese: the Mn in steel of the present invention still plays solution strengthening effect to material matrix, but add too low manganese and can cause red brittleness in steel processing, according to Product processing experience, technical solution of the present invention setting Mn content range is 0.08% ~ 0.13%, and this inventive features is control Mn/S ratio is 10-30.
Silicon: the Si in steel of the present invention is residual impurity element, technical solution of the present invention setting Si content≤0.03%.
Sulphur: the S in steel of the present invention is impurity element, according to processing request, Mn/S ratio is 10-30.Technical solution of the present invention setting S content 0.004 ~ 0.008%.
Phosphorus: the P in steel of the present invention is impurity element, too low P content can increase cost.Technical solution of the present invention setting P content≤0.015%.
In the present invention in manufacture method:
Slab heating temperature: ensure complete austenitizing and hot-work requirement, Heating temperature is that normal heating temperature is at 1150-1200 DEG C.
Finishing temperature: during hot rolling, material is perfect recrystallization rolling, cause mixed crystal in order to avoid material enters two-phase region rolling, cannot eliminate again in cold rolling process, finishing temperature is higher than Ar3 transformation temperature, through measuring static transformation point temperature at 890 DEG C, dynamic temperature decline 10-15 DEG C.Therefore the present invention sets finish rolling finishing temperature is 890 DEG C ~ 940 DEG C, according to product line ability, and can preferred 920-940 DEG C.
Coiling temperature: after hot rolling finish to gauge, austenite grain size and phase transformation grain-size after type of cooling decision rolling, can the growing up and homogenizing of austenite crystal after controlled rolling by air cooling, lower speed of cooling can control ferrite grain size and the solid solution capacity of carbon atom in ferrite, the raising of coiling temperature is simultaneously conducive to the abundant alligatoring of precipitate, and crystal grain is fully grown up.Therefore, after taking finish to gauge, air cooling is after 4 ~ 8 seconds, then is cooled to 741 ~ 760 DEG C with 15 ~ 30 DEG C/S speed and batches.
Compression ratio is rolled in acid: in conjunction with mill production, and compression ratio is normally set in 70%-90%.
Annealing temperature: control recovery and recrystallization and grain growth process by annealing process.By under research different time, annealing temperature is on the impact of performance, completing recrystallize at 15 seconds time material needs annealing temperature to be 770 degree, and after this along with the rising crystal grain of temperature is grown up gradually, when temperature reaches 850 degree, material yield strength reaches desired effects.Be conducive to ensureing that band steel is greater than 770 degree of annealing times so improve direct combustion section temperature, according to capacity of equipment, setting direct combustion section temperature 730 degree, to grow up requirement for reaching material ferrite crystal grain recrystallize simultaneously, soaking zone temperature setting 851 ~ 870 DEG C.Therefore, according to strip speed can the control cincture steel recrystallization annealing time at 15 ~ 34 seconds, direct combustion section temperature preferably 730 ~ 750 DEG C in the present invention, soaking zone temperature preferably 860 ~ 870 DEG C, preferably 25 ~ 34 seconds recrystallization annealing time.
Beneficial effect of the present invention: 1, the present invention is on existing Ti-IF steel constitution system basis, tested by technical study, design production technology difficulty little, scope holds the combination of manageable composition, compared with existing public technology, Nb element can not be added, belong to product and the technological design of low cost economy; 2, the present invention is annealing apart from short in conjunction with existing horizontal chamber oven, the feature that annealing time is short, by precisely controlling the rational Match of annealing time and temperature, overcome the deficiency of equipment, realizing the short period of time anneals and reaches ultra-deep and rush product requirement, produces line ability and is increased dramatically, through repetition test, under these processing condition, reach strong mechanical property, punching test is without the result of use of cracking; 3, the present invention is by the research at hot rolling technology, makes full use of hot rolling process temperature rule, obtains desirable hot-finished material tissue, for the annealing of horizontal chamber oven short period of time creates conditions, Rolling Production is simple, the reduction of cooling velocity after rolling, favourable minimizing cooling section cooling-water consumption; 4, segment distance of annealing under the present invention is based on horizontal chamber oven condition is short and carry out product and technical study, because annealing time is short, compared with vertical heater, realize high temperature annealing time shorten by becoming more meticulous of technique, annealing energy consumption significantly reduces, and can meet product requirement again simultaneously.
Steel of the present invention is a kind of under existing weaponry and equipment condition, by the research of product composition and technique, search out the technology that optimum control interval realizes the annealing of horizontal chamber oven short period of time, the steel plate microstructure grain size number that the ultra-deep adopting aforesaid method to produce rushes cold rolling hot dip galvanizing steel plate is I6.0 ~ I7.5 level, yield strength is 130 ~ 165MPa, tensile strength is 280 ~ 310MPa, and elongation after fracture A80mm is 40% ~ 47%.
The present invention is compared with Chinese patent 200710048926.8, its object is also realize deep drawing steel requirement, but its effect can only reach 180-190MPa level, this patent effect can not be reached, its carbon content scope, titanium add-on control and hot rolling after the type of cooling different from this patent, the grain fineness number of organizing after hot rolling is 11 grades, steel plate galvanized organizes grain fineness number 10.5 grades, completely not identical with organizing of obtaining of this patent.
Chinese patent: 201210141737.6 compare, its objective is and realize extra-deep drawing steel requirement, its production method is that vertical heater is produced, it adopts Nb-Ti-IF steel to design, its range set superiority is not be good at determining, add Nb element in composition and increase IF steel cost, annealing time reaches 200-600 second, and this method is that this patent institute is impracticable.
Chinese patent: 96190409.7 compare, its objective is that solution existing IF product made from steel Welding Area fatigue property does not reach and require problem, and adopt a kind of Ultra-low carbon aluminium killed steel not adding Ti or be not more than 0.0015%Ti, material welded heat affecting zone coarse grains is prevented by interpolation P and B element, the solid solution carbon strengthening crystal boundary of trace, improves material point welding zone fatigue property.Its chemical composition is Ultra-low carbon aluminium killed steel, there is solid solution carbon in base steel, this patent chemical composition is gapless atomic steel, Ti and C just by adding proper ratio generates compound, thus realize without solid solution carbon, reach ultra-deep rush object to reduce material yield strength, its chemical composition design principle is different from this patent, in embodiment, yield strength 157-227MPa does not reach the object of the invention yet, and its processing method implements the interval and very difficult degree guarantee of implementation result.
Accompanying drawing explanation
Fig. 1 is the metallographic structure photo that the ultra-deep of the embodiment of the present invention 1 rushes hot-rolled sheet.
Fig. 2 is the metallographic structure photo of the hot-rolled sheet of comparative example 3 of the present invention.
Fig. 3 is the metallographic structure photo that the ultra-deep of the embodiment of the present invention 1 rushes cold rolling hot dip galvanizing steel plate.
Fig. 4 is the metallographic structure photo of the lvanized cold rolled strip of comparative example 3 of the present invention.
Embodiment
Below in conjunction with embodiment 1-4, the invention will be further described, as shown in table 1 ~ table 4.
Table 1 the present invention (weight percent %), surplus is Fe and inevitable impurity.
By converter melting, RH stove vacuum decarburization, the continuously cast bloom of the chemical composition that obtains meeting the requirements, thickness is 210 ~ 240mm, and width is 800 ~ 1300mm, and length is 5000 ~ 10000mm.Scale slab is delivered to process furnace and is reheated, rolling Heating temperature is 1150 ~ 1200 DEG C, and the finish rolling stage is 7 passage finish rolling, carries out controlled cooling model, then batch, obtaining steel plate thickness is 2.0 ~ 4.0mm coils of hot-rolled steel, and with reference to Fig. 1, embodiment 1 technique obtains grain fineness number 6 grades of hot-rolled sheet tissues, structural constituent is ferrite+free cementite tissue, with reference to Fig. 2, adopt comparative example 3 technique to obtain grain fineness number 8 grades of hot-rolled sheet tissues, crystal grain is relatively tiny.Technology controlling and process is in table 2.
Table 2 hot rolling technology controling parameters of the present invention
By above-mentioned coils of hot-rolled steel again uncoiling after overpickling, reversible rolling or 5 Stands Cold Tandem Mills carry out cold rolling, cold rolling draft is 70% ~ 90%, the steel band rolling hard state after cold rolling is through horizontal chamber oven continuous annealing, and annealing process is: steel band in the annealing direct combustion section temperature 700 ~ 750 DEG C of horizontal chamber oven, soaking zone temperature 851 ~ 870 DEG C, 15 ~ 34 seconds recrystallization annealing time, pot galvanize, batches, and obtaining thickness is that the ultra-deep of 0.3 ~ 1.2mm rushes cold rolling hot dip galvanizing steel plate.Process control parameter is in table 3.
Table 3 the present invention is cold rolling, annealing process controling parameters
| Annealing | Direct combustion section temperature (DEG C) | Annealing temperature (DEG C) | Annealing time (s) |
| The present invention | 700～750 | 851～870 | 15～34 |
| Embodiment 1 | 703 | 860 | 23 |
| Embodiment 2 | 735 | 852 | 32 |
| Embodiment 3 | 722 | 862 | 27 |
| Embodiment 4 | 748 | 866 | 16 |
| Comparative example 1 | 685 | 835 | 30 |
| Comparative example 2 | 723 | 840 | 26 |
| Comparative example 3 | 730 | 856 | 30 |
| Comparative example 4 | 705 | 845 | 20 |
The mechanical property of the gap-free atom cold rolling hot dip galvanizing steel plate utilizing aforesaid method to obtain and grain fineness number are in table 4, with reference to Fig. 3, adopt embodiment 1 technique to obtain grain fineness number I6.5 level lvanized cold rolled strip tissue, structural constituent is ferrite+free cementite tissue, and its yield strength is 148Mpa.With reference to Fig. 4, adopt comparative example 3 technique to obtain grain fineness number 8 grades of hot-rolled sheet tissues, crystal grain is tiny, and its yield strength is 184MPa, and material yield strength is higher.
The mechanical property of table 4 gap-free atom cold rolling hot dip galvanizing of the present invention steel plate and grain fineness number
In addition to the implementation, the present invention can also have other embodiments.All employings are equal to the technical scheme of replacement or equivalent transformation formation, all drop on the protection domain of application claims.
Claims (5)
1. a short period of time annealing production ultra-deep rushes cold rolling hot dip galvanizing steel plate, chemical component weight per-cent is: C:0.0009% ~ 0.0018%, Si :≤0.03%, Mn:0.08% ~ 0.13%, Ti:0.030% ~ 0.062%, N:0.0018 ~ 0.0036%, S:0.004 ~ 0.008%, surplus is Fe and inevitable tramp element; According to formula 1 relation ratio X between control Ti constituent content and C, N, S constituent content: 1.3 ~ 2.0
According to formula 2 relation ratio Y:10 ~ 30 between control Mn constituent content and S constituent content
2. produce the method that ultra-deep described in claim 1 rushes cold rolling hot dip galvanizing steel plate, adopt desulfurizing iron, converter top bottom blowing, the refining of RH stove successively, be cast into continuous casting steel billet; Bar plate heating stove heating, roughing, finish rolling, batch obtain steel plate thickness be 2.0 ~ 4.0mm coils of hot-rolled steel; Then by coils of hot-rolled steel again uncoiling, through pickling, cold rolling, horizontal chamber oven continuous annealing, pot galvanize, batch that to obtain steel plate thickness be that the ultra-deep of 0.3 ~ 1.2mm rushes cold rolling hot dip galvanizing steel plate finished product, it is characterized in that, hot rolling technology adopts finishing temperature 890 ~ 940 DEG C, roll rear air cooling after 4 ~ 8 seconds, be cooled to 741 ~ 760 DEG C with 15 ~ 30 DEG C/S speed again to batch, cold-rolling process takes annealing direct combustion section temperature 700 ~ 750 DEG C, soaking zone temperature 851 ~ 870 DEG C, 15 ~ 34 seconds recrystallization annealing time.
3. the production method of a kind of gap-free atom cold rolling hot dip galvanizing steel plate as claimed in claim 2, it is characterized in that, described finish rolling end temp is 920 ~ 940 DEG C.
4. the production method of a kind of gap-free atom cold rolling hot dip galvanizing steel plate as claimed in claim 2, is characterized in that, described direct combustion section temperature 730 ~ 750 DEG C, soaking zone temperature 860 ~ 870 DEG C, 25 ~ 34 seconds recrystallization annealing time.
5. a kind of short period of time annealing production ultra-deep as claimed in claim 1 rushes cold rolling hot dip galvanizing steel plate, it is characterized in that: cold-rolling galvanization steel plate microstructure grain size number is I6.0 ~ I7.5 level, yield strength is 130 ~ 165MPa, tensile strength is 280 ~ 310MPa, and elongation after fracture A80mm is 40% ~ 47%.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112126881A (en) * | 2020-10-12 | 2020-12-25 | 马鞍山钢铁股份有限公司 | Deep-drawing-level hot-dip coated steel plate produced by short-time annealing and production method thereof |
| CN115386806A (en) * | 2022-09-13 | 2022-11-25 | 攀钢集团研究院有限公司 | Production method of hot-dip galvanized steel sheet suitable for high-speed continuous stamping and hot-dip galvanized steel sheet |
| CN115491583A (en) * | 2021-06-18 | 2022-12-20 | 上海梅山钢铁股份有限公司 | Ultra-deep drawing cold rolling hot-dip aluminum-zinc steel plate and manufacturing method thereof |
| CN115505832A (en) * | 2021-06-07 | 2022-12-23 | 上海梅山钢铁股份有限公司 | Hot-dip aluminum-zinc steel plate for liquid crystal backboard with yield strength of 340MPa |
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| CN115505832A (en) * | 2021-06-07 | 2022-12-23 | 上海梅山钢铁股份有限公司 | Hot-dip aluminum-zinc steel plate for liquid crystal backboard with yield strength of 340MPa |
| CN115505832B (en) * | 2021-06-07 | 2023-09-05 | 上海梅山钢铁股份有限公司 | Hot-dip aluminum zinc-plated steel plate with yield strength of 340MPa for liquid crystal backboard |
| CN115491583A (en) * | 2021-06-18 | 2022-12-20 | 上海梅山钢铁股份有限公司 | Ultra-deep drawing cold rolling hot-dip aluminum-zinc steel plate and manufacturing method thereof |
| CN115491583B (en) * | 2021-06-18 | 2023-09-05 | 上海梅山钢铁股份有限公司 | Ultra-deep drawing cold-rolled hot-dip aluminum-zinc steel plate and manufacturing method thereof |
| CN115386806A (en) * | 2022-09-13 | 2022-11-25 | 攀钢集团研究院有限公司 | Production method of hot-dip galvanized steel sheet suitable for high-speed continuous stamping and hot-dip galvanized steel sheet |
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