CN102758132B - Method for manufacturing deep-drawing steel with high r value through continuous annealing of micro-carbon aluminum killed steel - Google Patents
Method for manufacturing deep-drawing steel with high r value through continuous annealing of micro-carbon aluminum killed steel Download PDFInfo
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Abstract
The invention relates to a method for manufacturing deep-drawing steel with high r value through continuous annealing of micro-carbon aluminum killed steel, belonging to the technical field of metallurgical sheet production. A technical scheme is as follows: the method comprises the procedures of smelting and hot rolling, wherein in the smelting procedure, the aluminum killed steel comprises the following chemical components in percentage by mass: 0.01-0.02% of C (Carbon), not more than 0.006% of Si (Silicon), 0.12-0.18% of Mn (Manganese), not more than 0.01% of P (Phosphorus), not more than 0.015% of S (Sulfur), 0.025-0.06% of Als (Aluminum), not more than 0.004% of N (Nitrogen) and the balance of Fe (Ferrum). The method for manufacturing the deep-drawing steel with high r value through continuous annealing of the micro-carbon aluminum killed steel, provided by the invention, has the advantages that no micro alloy element is additionally added, the components of the traditional aluminum killed steel are improved and contents of C and Si are reduced; by means of improving steel smelting and hot rolling processes, a deep-drawing cold rolled sheet with low yield strength and high elongation rate is manufactured and has the advantages of low cost and good performance; and mechanical performance indexes of a finished product are as follows: yield strength is about 175 MPa, tensile strength is about 290 MPa, elongation rate is not less than 40%, n is about 0.2 and r value is not less than 2.00 or so.
Description
Technical field
The present invention relates to the micro-carbon aluminium killed steel of a kind of use and even move back and produce the method for steel for high r value deep-draw, belong to metallurgical plate production technical field.
Technical background
The deep-draw of high r value with the definition of steel is: r >=2.0, the cold rolled sheet of using for deep-draw.At present, production deep-draw rank steel band DC04 is mainly used IF steel, and in IF steel, impurity is less, connects to move back rapid heating, and in the equal thermal process of high temperature, ferritic free, in growing up, connects that to step back IF steel yield strength low, and n, r value are high, and deep drawing quality is good.But, IF steel C content low (general C≤0.005%), RH decarburization time is long, and need to add the alloys such as Ti, Nb, and cost is higher.Traditional carbon aluminium-killed steel cost is lower, but because C content is high, connects and move back C and Fe formation Fe in ag(e)ing process
xc(x:2～3).Even moving back the carbide forming in ag(e)ing process has very strong precipitation strength effect for these, has improved the yield strength of steel band, has reduced toughness and the deep drawing quality of steel plate.For improving to connect, move back the mechanical property of producing aluminium killed steel, at present, the aluminium killed steel that even moves back production generally adds B, and owing to adding alloy, increases cost on the one hand containing the aluminium killed steel of B, and micro-B content control has increased steel-making difficulty on the other hand.
Summary of the invention
The object of this invention is to provide the micro-carbon aluminium killed steel of a kind of use and connect the method for steel for high r value deep-draw of producing of moving back, do not add in addition microalloy element, improved the composition of conventional aluminum killed steel, C, Si content have been reduced, by improvement make steel, hot rolling technology, produce that a kind of yield strength is low, unit elongation is high, n and the high deep-draw cold-reduced sheet of r value, cost is low, performance is good, solves the problems referred to above that background technology exists.
Technical scheme of the present invention is:
The micro-carbon aluminium killed steel of a kind of use connects the method for steel for high r value deep-draw of producing of moving back, comprise smelting, hot rolling, cold-rolling continuous annealing operation, in smelting procedure, the mass percent of aluminium killed steel chemical composition is: C:0.01～0.02%, Si≤0.006, Mn:0.12～0.18, P≤0.01%, S≤0.015%, Als:0.025～0.06%, N≤0.004%, remains as Fe.
In described smelting procedure, converter control is as follows: on average pack 25 tons/stove of steel scrap into, molten steel quality is than more than 90%; Basicity of slag is pressed 4.0-4.5 and is controlled, the low-sulfur lime that converter smelting is used sulphur content to be less than 0.03%, and the active oxidation calcium contents of lime is greater than 90%, granularity 5～60mm; Bessemerize terminal requirement [C]≤0.05%, [P] < 0.008%, [S]≤0.008%, terminal temperature is controlled at 1700 ± 10 ℃, controls terminal oxygen 500～950ppm, ensures the RH requirement of entering the station; The stable tap of controlling, ladle headroom 300mm, provides suitable ladle space for RH processes; Two pushing off the slag before and after tapping process, the quantity of slag under strict control; With respect to converter molten steel Intake Quantity, in tapping process, to add mass percent be that the aluminium slag of 0.009～0.0011% fluorite, 0.0020～0.0023% lime and 0.0014～0.0018% is as top slag modifier to every stove.
In described smelting procedure, RH vacuum processing time is calculated and is obtained by mass transfer Equation Theory, and the treatment time is 20-33 minute, pure degassed 5--12 minute, final vacuum≤1.05mbar; Decarburization finishes rear aluminum deoxidation, adds high carbon ferromanganese to regulate manganese content; Guarantee that molten steel opens during watering and keep molten steel calmness 30～60 minutes to continuous casting after RH processing finishes, the inclusion fully floating in molten steel, with pure molten steel.
Described hot-rolled process, requires low-temperature heat, high-temperature final rolling, high temperature coiling;
A, hot rolling Heating temperature are 1180-1220 ℃;
B, finish rolling start rolling temperature are 1050-1080 ℃;
C, finishing temperature are 880-910 ℃;
D, coiling temperature are 650-700 ℃;
In e, course of hot rolling, roughing stay-warm case normally drops into, needless to say warm after roughing finishes.
Described cold-rolling continuous annealing operation,
A, acid are rolled draft and are controlled at 75～82%;
It is 800～860 ℃ that soaking temperature is moved back by b, company, soaking time 80～180s.Slow cooling final cooling temperature is 680-730 ℃.Aging temp is 400 ± 50 ℃, aging time: 4～15min.Production belt speed is between 71～313m/min, and belt speed must be mated mutually with thickness;
C, smooth unit elongation are set as 0.6-1.2%, and smooth unit elongation must mate mutually with thickness.
Positively effect of the present invention: do not add in addition microalloy element, improved the composition of conventional aluminum killed steel, reduced C, Si content, by improvement make steel, hot rolling technology, produce the deep-draw cold-reduced sheet that a kind of yield strength is low, unit elongation is high, cost is low, and performance is good, finished product mechanical performance index: finished product mechanical performance index: the about 175MPa of yield strength, the about 290MPa of tensile strength, unit elongation >=40%, n approximately 0.2, r value approximately >=2.2.
Embodiment
Below in conjunction with embodiment, further illustrate the present invention.
In an embodiment, comprise smelting, hot rolling, cold-rolling continuous annealing operation.
1, smelting procedure: converter---RH smelts
Embodiment is as shown in table 1 with steel chemical composition.
Table 1 chemical composition
(chemical composition: wt%)
Embodiment 1,2, and converter packs desulphurised hot metal into and is respectively 270,273 tons.With respect to converter molten steel Intake Quantity, in tapping process, to add mass percent be that the aluminium slag of 0.00107% fluorite, 0.00214% lime and 0.0016% is as top slag modifier to every stove.
Basicity of slag is controlled by 4.5, and RH vacuum processing time is respectively 26,25 minutes, and the pure degassed time is respectively 10,12 minutes, final vacuum 1.00mbar.RH vacuum processing technique calculates according to Mass Transfer Model.
Lower C content moves back the company of making the carbide decreases of separating out in process, and Ar1, Ar3 temperature rise.Lower Si content can obviously reduce surrender, the tensile strength of steel, improves the toughness of steel.Reasonably Als content is conducive to fixing middle steel grade N, thereby forms the solution strengthening effect that AlN reduces N, improves the toughness of steel.
2, hot-rolled process: 1200 ± 20 ℃ of Heating temperatures, heat-up time 40min, finish rolling start rolling temperature is 1050 ± 10 ℃, 900 ± 10 ℃ of finishing temperatures, 700 ± 10 ℃ of coiling temperatures.Hot-rolled finished product specification is two volume 1275 * 5.5mm.Concrete technology parameter is in Table 2.
Table 2 hot-rolled process parameter
Lower Heating temperature has guaranteed that continuous casting is cooled to the AlN forming in room temperature process and does not dissolve.Higher coiling temperature will make the further slaking of AlN.Thick AlN particle N content in reducing steel simultaneously, reduces it to ferritic anchoring in subsequent anneal process, is conducive to obtain thick ferritic structure.
3, cold-rolling continuous annealing operation: band steel acid is rolled trimmed size and is the acid of 1250 * 0.8mm, B band steel and rolls trimmed size and be 1250 * 0.7mm, and cold rolling draft is respectively 80%.
Concrete continuous annealing process is in Table 3.
Table 3 continuous annealing process
This is manufactured experimently smooth unit elongation and is set as 0.65%.
C content is 0.01～0.02 o'clock, 730～770 ℃ of Ar1 temperature ranges.When soaking temperature is 850 ℃, steel band is in two-phase region, now be organized as ferrite+austenite.Fast owing to even moving back rate of heating, soaking time is short, in two-phase region, not becoming mutually austenitic ferrite crystal grain grows up continuing, and because C solid solubility in ferrite is less than C solid solubility in austenite, C content in ferrite will spread to austenite, thereby reduce thick ferritic C content in two-phase region.When soaking finishes to enter slow cooling section, because temperature declines, will there is ferrite transformation in the austenite of phase transformation, and oversaturated C will form Fe
3c particle.Because slow cooling section is in temperature-fall period, and the time is short, and the ferrite of phase transformation cannot fully be grown up, and finally forms the tissue that thick ferrite mixes with tiny ferrite.Fast cold junction Shu Houjin enters aging section, and under the aging temp of 400 ℃, in ferrite, oversaturated C further separates out and forms Fe
xc(x:2～3).While there is deformation, thick ferrite is larger by grain-size, and C content is low, and precipitate is few, thereby reaches by first there is surrender the effect that reduces yield strength.
Mechanical property is in Table 4.
Table 4 mechanical property
In table 4, mechanical property meets in GB GB/T5213-2008 completely about the relevant mechanical property requirements of steel DC04 for deep-draw.
Claims (3)
1. one kind connects with micro-carbon aluminium killed steel the method for steel for high r value deep-draw of producing of moving back, it is characterized in that comprising smelting, hot rolling, cold-rolling continuous annealing operation, in smelting procedure, the mass percent of aluminium killed steel chemical composition is: C:0.01～0.02%, Si≤0.006, Mn:0.12～0.18, P≤0.01%, S≤0.015%, Als:0.025～0.06%, N≤0.004%, remains as Fe; Described cold-rolling continuous annealing operation,
A, acid are rolled draft and are controlled at 75～82%;
It is 800～860 ℃ that soaking temperature is moved back by b, company, soaking time 80～180s;
?slow cooling final cooling temperature is 680-730 ℃;
Aging temp is 400 ± 50 ℃, aging time 4～15min;
Production belt speed is between 71～313m/min, and belt speed must be mated mutually with thickness;
C, smooth unit elongation are set as 0.6-1.2%, and smooth unit elongation must mate mutually with thickness.
2. the micro-carbon aluminium killed steel of a kind of use even moves back and produces the method for steel for high r value deep-draw according to claim 1, it is characterized in that in described smelting procedure:
A, bessemerize terminal requirement [C]≤0.05%, terminal temperature is controlled at 1700 ± 10 ℃, controls terminal oxygen: 500～950ppm;
B, RH vacuum processing time be at 20-33 minute, pure degassed 5-12 minute, final vacuum≤1.05mbar; Decarburization finishes rear aluminum deoxidation, for guaranteeing that C content is not less than lower limit requirement, adds high carbon ferromanganese to regulate manganese content, carbon content;
C, guarantee that molten steel opens during watering and keep molten steel calmness 30～60 minutes to continuous casting after RH processing finishes, the inclusion fully floating in molten steel, with pure molten steel;
D, with respect to converter molten steel Intake Quantity, in tapping process, to add mass percent be that the aluminium slag of 0.009～0.0011% fluorite, 0.0020～0.0023% lime and 0.0014～0.0018% is as top slag modifier to every stove.
3. the micro-carbon aluminium killed steel of a kind of use even moves back and produces the method for steel for high r value deep-draw according to claim 1, it is characterized in that described hot-rolled process, requires low-temperature heat, high-temperature final rolling, high temperature coiling;
A, hot rolling Heating temperature are 1180-1220 ℃;
?b, finish rolling start rolling temperature are 1050-1080 ℃;
C, finishing temperature are 880-910 ℃;
D, coiling temperature are 650-700 ℃;
In e, course of hot rolling, roughing stay-warm case normally drops into, needless to say warm after roughing finishes.
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| CN102978505B (en) * | 2012-11-20 | 2014-11-19 | 首钢总公司 | Smelting method of high-strength IF steel |
| CN104372242B (en) * | 2014-10-10 | 2017-05-17 | 河北钢铁股份有限公司邯郸分公司 | 470MPa grade cold rolled strip steel and production method thereof |
| CN104294147B (en) * | 2014-10-30 | 2016-08-24 | 武汉钢铁(集团)公司 | Super high-strength cable steel and production method thereof |
| TWI595099B (en) * | 2017-03-03 | 2017-08-11 | 中國鋼鐵股份有限公司 | Low yield ratio steel material and method of producing the same |
| CN110438329B (en) * | 2019-07-23 | 2022-07-19 | 北京首钢股份有限公司 | Method for eliminating skin warping defect of boron-containing low-carbon aluminum killed steel strip |
| CN114645132B (en) * | 2020-07-14 | 2023-11-17 | 柳州钢铁股份有限公司 | Continuous annealing SPCC steel belt with performance close to that of cover annealing product |
| CN112746223B (en) * | 2020-12-30 | 2022-02-01 | 广西柳钢华创科技研发有限公司 | High-r-value low-carbon aluminum killed steel produced by ferrite rolling process |
| CN112899562A (en) * | 2021-01-15 | 2021-06-04 | 山东钢铁集团日照有限公司 | Micro-carbon hot-dip galvanized steel strip with stable yield strength control and production method thereof |
| CN113122690B (en) * | 2021-04-16 | 2022-03-22 | 攀钢集团攀枝花钢铁研究院有限公司 | Low-delta r-value micro-carbon steel cold-rolled steel plate and preparation method thereof |
| CN114686665A (en) * | 2022-03-16 | 2022-07-01 | 安阳钢铁集团有限责任公司 | Anti-aging mild steel deep-drawing strip steel and production method thereof |
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