CN104233062B - 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 time annealing production ultra-deep rushes hot-dip galvanizing sheet steel and its production method, micro- group of its steel plate
It is I6.0～I7.5 levels to knit grain size number, and yield strength is 130～165MPa, and tensile strength is 280～310MPa, has no progeny and stretches
Long rate A80mm is 40%～49%, it is adaptable to which household appliances, five metals have ultra-deep punching forming processing request part, material yield
Low intensity, shaping reliability are high.
Background technology
As domestic household electrical appliances, hardware industry product structure design are continued to optimize, increasing spare and accessory parts show as knot
Structure is complicated, and molding difficulty is big, at the same the raising of forming requirements to raw material it is also proposed that higher and higher requirement, household appliances purposes
In, galvanizing product purpose is most wide, and because its zinc layers material ductility is good, hot dip zinc product has extraordinary processability, together
Intermittent fever galvanizing production has very good corrosion resisting property and relatively low cost, and deep draw galvanizing production obtains extensively should in household electric appliances
With.
Its raw material of deep-draw cold rolling hot dip galvanizing product is designed using equal IF component systems, and usual IF steel is divided into Ti-IF, Nb-Ti-
IF and Nb-IF steel, wherein Ti-IF costs are minimum, and its recrystallization annealing temperature is also minimum, are that deep punching steel product design is first
Choosing.Deep-draw cold rolling hot dip galvanizing product is the direct hot dip after continuous annealing process, continuous annealing furnace point in existing production technology
For vertical heater and horizontal chamber furnace (oven), which main difference is that annealing temperature and annealing time differ greatly, because of vertical heater annealing segment length, can be real
Existing long period annealing time, is easy to get the galvanizing production of deep drawability, usual annealing time not as technical protection point, but
For horizontal chamber furnace (oven) short time annealing production deep punching steel data seldom, solution is disclosed especially for production extra-deep drawing steel and also do not had
Have.
Chinese patent：200710048926.8, the production method of deep drawing skin-passed hot-dip galvanizing sheet steel discloses deep drawing skin-passed heat
The production method of galvanized steel plain sheet, its carbon content scope 0.0030-0.0060%, Ti-3.4N-4C-1.5S content range 0.02-
0.04%, it is cooled to 700-780 DEG C soon after rolling, anneals in 780～880 DEG C of temperature ranges, obtain product yield strength 185-
190MPa, tensile strength 310-320MPa, percentage elongation A8041-43%, finished product grain size are 10.5 grades, and the patent effect is not up to
To the object of the invention, its process implementing temperature range is larger, the bad determination of implementation result.
Chinese patent：201210141737.6, the compound ultra-deep punching galvanized sheet of a kind of Nb, Ti 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, balance of Fe；Annealing temperature 850-860 DEG C, annealing
Second time 200-600, final products yield strength≤155MPa, tensile strength are 260～330MPa, and elongation percentage >=44% should
Patent effect can reach ultra-deep punching performance requirement, and which has the disadvantage to design for Nb-Ti-IF, relatively costly, and the addition of Nb causes material
Annealing difficulty is increased, and annealing time is up to the 200-600 seconds, and the technology cannot be implemented in the inventive method.
Chinese patent：96190409.7, with the ultralow carbon cold-rolled steel plate and galvanized steel plain sheet and its life that improve fatigue behaviour
Production. art, steel plate contain percentage by weight：0.0001-0.0026%C, most 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, remaining is
Fe and inevitable impurity, its process are to roll to be cooled to hot rolled strip with 50 DEG C/sec of rate of cooling in rear 1.5S
750 DEG C, cold-rolled strip carries out continuous annealing at 600-900 DEG C.The patent is to solve existing IF product made from steel Welding Area fatigue
Performance does not reach the problem of requirement, and its chemical composition is Ultra-low carbon aluminum killed steel, surrenders 157-227MPa, do not reach in embodiment
The object of the invention.It is room temperature to 750 DEG C that its technique is coiling temperature, and annealing temperature is 600-900 DEG C, and scope is big, it is impossible to select
Select reasonable implementation interval and ensure implementation result.
The content of the invention
It is an object of the invention to provide a kind of short time annealing production ultra-deep rushes hot-dip galvanizing sheet steel and its production method, mainly
Solve prior art in using horizontal furnace annealing production ultra-deep rush hot-dip galvanizing sheet steel, because annealing time it is short, product ultra-deep punching performance
The technical problem of requirement is not reached.
The present invention is studied through long-term experiment, finds product composition, the relation of process and performance, solves the punching of short time ultra-deep
A production technology difficult problem for hot dip.Technical thought is：Design be suitable for the short time annealing component system, by low-carbon (LC), low manganese and
The addition of suitable titanium elements, reaches fixed steel carbon, nitrogen, the purpose of sulfur, reduces carbon, the solid solution strengthening effect of manganese element, while
Thick carbon nitrogen sulfur titanium compound can be separated out again reduces annealing recrystallization temperature, and the short time completes material recrystallization annealing and controls crystalline substance
Grain length is big, reaches the low surrender ultra-deep strategically important place of product and asks.
To reach above-mentioned purpose, the chemical composition (percentage by weight) 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%, balance of Fe and inevitable tramp element.Wherein Ti/ (4C+3.4N+1.5S)
Ratio 1.3-2.0, Mn/S ratio 10-30.
Short time annealing production ultra-deep of the present invention is rushed hot-dip galvanizing sheet steel chemical composition and is limited within the above range
Reason is as follows：
Carbon：In product of the present invention, it is desirable to which carbon content is more low better, because carbon solid solution in steel is played reinforcing and is made to matrix
With, at the same the carbide that formed of carbon and titanium also can some invigoration effect, it is strong to product surrender by studying different carbon contents
The impact of degree, when carbon content is more than 0.0020%, material yield strength is significantly improved, and too low carbon content production difficulty is larger,
Therefore, technical solution of the present invention sets C content scope as 0.0009%～0.0018%.
Nitrogen：In ultra-deep rushes cold rolling hot dip galvanizing steel plate, nitrogen and carbon equally play reinforcing to matrix, to steel plate deep drawability not
Profit, it is desirable to which nitrogen content is more low better, and the same production difficulty of too low nitrogen content is big.Technical solution of the present invention sets N content
0.0018～0.0036%.
Titanium：By the addition of Ti, further combine with C, N, S atom, generate the carbon nitrogen sulfur compound of Ti, so as to eliminate trip
From C, N atom, realize that gapless solid solution atom is present in steel.The content of titanium is related to carbon, nitrogen, sulfur content, is sent out by research
When existing Ti/ (4C+3.4N+1.5S) ratio is too low, steel are carried on as before and have carbon, nitrogen-atoms fix very well to cause the strength of materials to improve,
Because the raising of material recrystallization temperature causes annealing, because of the time, not enough not reaching ultra-deep rushes low surrender when the ratio is too high simultaneously
Effect, therefore, technical solution of the present invention sets Ti contents as 0.030%～0.062%, and the inventive features are control Ti/ (4C+
3.4N+1.5S) ratio be 1.3-2.0.
Manganese：Mn in steel of the present invention still plays solution strengthening effect to material matrix, but the too low manganese of addition can cause steel
Red brittleness in material processing, according to Product processing experience, technical solution of the present invention sets Mn content ranges as 0.08%～0.13%,
The inventive features are to control Mn/S ratios for 10-30.
Silicon：Si in steel of the present invention be residual impurity element, technical solution of the present invention setting Si content≤0.03%.
Sulfur：S in steel of the present invention is impurity element, and according to processing request, Mn/S ratios are 10-30.The technology of the present invention side
Case setting S contents 0.004～0.008%.
Phosphorus：P in steel of the present invention is impurity element, and too low P content can increase cost.Technical solution of the present invention sets P
Content≤0.015%.
In the present invention in manufacture method：
Slab heating temperature：Ensure that complete austenitizing and hot-working require that heating-up temperature exists for normal heating temperature
1150-1200℃。
Finishing temperature：During hot rolling, material is perfect recrystallization rolling, in order to avoid material causes to mix into two-phase section rolling
Crystalline substance, cannot be eliminated during cold rolling again, and finishing temperature is higher than Ar3 transformation temperatures, exist through determining static transformation point temperature
890 DEG C, dynamic temperature declines 10-15 DEG C.Therefore the present invention sets finish rolling finishing temperature as 890 DEG C～940 DEG C, according to producing line energy
Power, preferable 920-940 DEG C.
Coiling temperature：After hot rolling finish to gauge, the type of cooling determines austenite grain size and phase transformation crystallite dimension after rolling, leads to
Cross austenite crystal after air cooling can control rolling to grow up and homogenization, the controllable ferrite grain size of relatively low rate of cooling and
Solid solution capacity of the carbon atom in ferrite, while the raising of coiling temperature is conducive to precipitate to be fully roughened, 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 batched.
Compression ratio is rolled in acid：With reference to mill production, compression ratio is normally set in 70%-90%.
Annealing temperature：Recovery and recrystallization and grain growth process are controlled by annealing process.By studying under different time
Impact of the annealing temperature to performance, completing recrystallization in 15 seconds time material needs annealing temperature for 770 degree, hereafter with temperature
Rising crystal grain gradually grow up, when temperature reaches 850 degree, material yield strength reaches desired effectss.So improving direct combustion section
Temperature advantageously ensures that strip steel more than 770 degree annealing times, according to capacity of equipment, sets 730 degree of direct combustion section temperature, at the same be up to
Requirement of growing up is recrystallized to material ferrite crystal grain, soaking zone temperature sets 851～870 DEG C.Therefore, according to strip speed
The controllable strip steel recrystallization annealing time at 15～34 seconds, the present invention in preferably 730～750 DEG C of direct combustion section temperature, soaking zone temperature
Preferably 860～870 DEG C of degree, preferably 25～34 seconds recrystallization annealing time.
Beneficial effect of the present invention：1st, the present invention is tested by technical study on the basis of existing Ti-IF steel constitutions system,
Design that production technology difficulty is little, scope be easily controlled into subassembly, compared with existing public technology, can be first without Nb
Element, belongs to inexpensive economic product and technological design；2nd, the present invention be with reference to existing horizontal furnace annealing apart from short, during annealing
Between it is short the characteristics of, by the Proper Match for being precisely controlled annealing time and temperature, overcome the deficiency of equipment, realize that the short time moves back
Fight and reached ultra-deep and rush product requirement, producing line ability is increased dramatically, and through repetition test, under this process conditions, reaches
Strong mechanical property, using effect of the punch test without cracking are arrived；3rd, the present invention is by the research in hot rolling technology, fully sharp
With hot rolling process temperature rule, preferable hot-finished material tissue is obtained, be that the annealing of horizontal chamber furnace (oven) short time creates conditions, rolling life
Simple, the reduction of cooling velocity after rolling is produced, it is favourable to reduce cooling section cooling-water consumption；4th, the present invention is moved back under the conditions of being based on horizontal chamber furnace (oven)
Fiery segment distance is short and carries out product and technical study, due to annealing time it is short, compared with vertical heater, by the reality that becomes more meticulous of technique
The existing high annealing time shortens, and annealing energy consumption is greatly reduced, while and can meet product requirement.
Steel of the present invention is a kind of under the conditions of existing weaponry and equipment, by the research of product composition and technique, searches out optimal control
The technology of horizontal chamber furnace (oven) short time annealing is realized in system interval, and the ultra-deep produced using said method rushes the steel plate of cold rolling hot dip galvanizing steel plate
Microscopic structure grain size number is I6.0～I7.5 levels, and yield strength is 130～165MPa, and tensile strength is 280～310MPa,
Elongation after fracture A80mm is 40%～47%.
Compared with Chinese patent 200710048926.8, its purpose is also to realize deep punching steel requirement to the present invention, but its effect
180-190MPa levels are can only achieve, this patent effect can not be reached, its carbon content scope, after the control of titanium addition and hot rolling
The type of cooling is different from this patent, and the tissue grain size after hot rolling is 11 grades, galvanized steel plain sheet 10.5 grades of grain size of tissue, with this specially
The tissue that profit is obtained is differed completely.
Chinese patent：201210141737.6 compare, and its objective is to realize extra-deep drawing steel requirement, and its production method is vertical
Stove is produced, and which adopts Nb-Ti-IF steel to design, and its range set superiority is not to be good at determining, adds Nb elements to increase in composition
IF steel costs, annealing time are up to the 200-600 seconds, and this method is that this patent institute is impracticable.
Chinese patent：96190409.7 compare, and its objective is that solving existing IF product made from steel Welding Area fatigue behaviour does not reach
Requirement problem, and adopt a kind of without Ti or the no more than Ultra-low carbon aluminum killed steel of 0.0015%Ti, it is first by adding P and B
Element prevents material welding heat affected zone coarse grains, micro solid solution carbon reinforcing crystal boundary from improving material Welding Area fatigue behaviour.Its
Chemical composition is Ultra-low carbon aluminum killed steel, and base steel has solid solution carbon, and this patent chemical composition is gapless atomic steel, is exactly based on
Ti and the C generation compound of addition proper ratio, so as to realize without solid solution carbon, to reduce material yield strength and reach ultra-deep rushing mesh
, its Design of Chemical Composition principle is different from this patent, and in embodiment, yield strength 157-227MPa does not reach this yet
Improving eyesight, its process is implemented interval and implementation result degree of being difficult and is ensured.
Description of the drawings
Fig. 1 is the metallographic structure photo that the ultra-deep of the embodiment of the present invention 1 rushes hot rolled plate.
Fig. 2 is the metallographic structure photo of the hot rolled plate of comparative example of the present invention 3.
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 of the present invention 3.
Specific embodiment
With reference to embodiment 1-4, the invention will be further described, as shown in 1～table of table 4.
Table 1 (percentage by weight %) of the invention, balance of Fe and inevitable impurity.
By converter melting, RH stove vacuum decarburizations, the continuous casting billet of the chemical composition that obtains meeting the requirements, thickness is 210～
240mm, width are 800～1300mm, and length is 5000～10000mm.Scale slab delivers to heating furnace reheating, rolling heating
Temperature is 1150～1200 DEG C, and the finish rolling stage is 7 passage finish rolling, is controlled cooling, is then batched, obtains steel plate thickness
For 2.0～4.0mm coils of hot-rolled steel, with reference to Fig. 1,1 technique of embodiment obtains 6 grades of hot rolled plate tissues of grain size, and structural constituent is ferrum
Ferritic+free cementite tissue, with reference to Fig. 2, obtains 8 grades of hot rolled plate tissues of grain size, crystal grain relatively thin using 3 technique of comparative example
It is little.Technology controlling and process is shown in Table 2.
2 hot rolling technology control parameter of the present invention of table
By above-mentioned coils of hot-rolled steel again uncoiling after pickling, carry out on reversible rolling or 5 Stands Cold Tandem Mills it is cold rolling,
Cold rolling reduction ratio be 70%～90%, it is cold rolling after the steel band for rolling hard state through horizontal chamber furnace (oven) continuous annealing, annealing process is：
Annealing direct combustion section temperature 700～750 DEG C of the steel band in horizontal chamber furnace (oven), 851～870 DEG C of soaking zone temperature, recrystallization annealing time 15
～34 seconds, galvanizing was batched, and is obtained the ultra-deep that thickness is 0.3～1.2mm and is rushed cold rolling hot dip galvanizing steel plate.Process control parameter is shown in
Table 3.
3 cold rolling, annealing process control parameter of the invention of table
| 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 and grain size of the gap-free atom cold rolling hot dip galvanizing steel plate obtained using said method is shown in Table 4, ginseng
According to Fig. 3, grain size I6.5 level lvanized cold rolled strip tissue is obtained using 1 technique of embodiment, structural constituent is ferrite+free carburizing
Body is organized, and its yield strength is 148Mpa.With reference to Fig. 4,8 grades of hot rolled plate tissues of grain size, crystal grain are obtained using 3 technique of comparative example
Tiny, its yield strength is 184MPa, and material yield strength is higher.
The mechanical property and grain size of 4 gap-free atom cold rolling hot dip galvanizing steel plate of the present invention of table
In addition to the implementation, the present invention can also have other embodiment.All employing equivalents or equivalent transformation shape
Into technical scheme, all fall within the protection domain of application claims.
Claims (3)
1. it is a kind of to produce the method that ultra-deep rushes cold rolling hot dip galvanizing steel plate, successively using desulfurizing iron, converter top bottom blowing, RH
Stove refine, it is cast into continuous casting steel billet；Heating of plate blank stove heat, roughing, finish rolling, batch acquisition steel plate thickness be 2.0～4.0mm it is hot
Rolled steel coils；Then by coils of hot-rolled steel again uncoiling, Jing pickling, cold rolling, horizontal chamber furnace (oven) continuous annealing, galvanizing, batch and obtain steel plate
Thickness is that the ultra-deep of 0.3～1.2mm rushes cold rolling hot dip galvanizing steel plate finished product, be it is characterized in that, continuous casting steel billet chemical component weight percentage
Than for：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%, balance of Fe and inevitable tramp element；Controlled according to formula 1
Relation ratio X between Ti constituent contents processed and C, N, S constituent content：
According to the relation ratio Y between 2 controlled Mn constituent contents of formula and S constituent contents：Hot rolling technology
Using 890～940 DEG C of finish rolling end temp, after rolling rear air cooling 4～8 seconds, then 741～760 are cooled to 15～30 DEG C/S speed
DEG C batched, cold-rolling process takes 700～750 DEG C of annealing direct combustion section temperature, 851～870 DEG C of soaking zone temperature, and recrystallization is moved back
15～34 seconds fiery time.
2. the method that production ultra-deep as claimed in claim 1 rushes cold rolling hot dip galvanizing steel plate, is characterized in that, the finish rolling terminates temperature
Spend for 920～940 DEG C.
3. the method that production ultra-deep as claimed in claim 1 rushes cold rolling hot dip galvanizing steel plate, is characterized in that, the direct combustion section temperature
730～750 DEG C, 860～870 DEG C of soaking zone temperature, 25～34 seconds recrystallization annealing time.
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| 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 |
| 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 |
| 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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| JPS6376848A (en) * | 1986-09-19 | 1988-04-07 | Kawasaki Steel Corp | Cold rolled steel sheet for extra deep drawing and its manufacture |
| US4931106A (en) * | 1987-09-14 | 1990-06-05 | Kawasaki Steel Corporation | Hot rolled steel sheet having high resistances against secondary-work embrittlement and brazing embrittlement and adapted for ultra-deep drawing and a method for producing the same |
| US5041166A (en) * | 1989-09-11 | 1991-08-20 | Kawasaki Steel Corporation | Cold-rolled steel sheet for deep drawing and method of producing the same |
| JPH09157788A (en) * | 1995-12-08 | 1997-06-17 | Kobe Steel Ltd | Hot rolled steel sheet for deep drawing excellent in secondary working brittleness resistance |
| JPH09310149A (en) * | 1996-05-21 | 1997-12-02 | Kobe Steel Ltd | Cold rolled steel sheet excellent in deep drawability, spot weldability and punchability and its production |
| JP3572883B2 (en) * | 1997-08-26 | 2004-10-06 | 住友金属工業株式会社 | Manufacturing method of cold rolled steel sheet with small in-plane anisotropy and excellent secondary work brittleness resistance |
| JP4177477B2 (en) * | 1998-04-27 | 2008-11-05 | Ｊｆｅスチール株式会社 | Manufacturing method of cold-rolled steel sheet and hot-dip galvanized steel sheet with excellent room temperature aging resistance and panel characteristics |
| US6361624B1 (en) * | 2000-09-11 | 2002-03-26 | Usx Corporation | Fully-stabilized steel for porcelain enameling |
| KR20100134547A (en) * | 2010-12-15 | 2010-12-23 | 주식회사 포스코 | Enameling steel sheet and manufacturing method thereof |
| KR101368576B1 (en) * | 2011-10-28 | 2014-03-03 | 현대제철 주식회사 | Cold-rolled steel sheet and method of manufacturing the same |
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