CN102758129B - Method for manufacturing non-spangle galvanized sheet DX54D+Z from aluminum killed steel - Google Patents
Method for manufacturing non-spangle galvanized sheet DX54D+Z from aluminum killed steel Download PDFInfo
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- CN102758129B CN102758129B CN 201210202941 CN201210202941A CN102758129B CN 102758129 B CN102758129 B CN 102758129B CN 201210202941 CN201210202941 CN 201210202941 CN 201210202941 A CN201210202941 A CN 201210202941A CN 102758129 B CN102758129 B CN 102758129B
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Abstract
The invention relates to a method for manufacturing a non-spangle galvanized sheet DX54D+Z from 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, hot rolling, cold rolling and galvanizing, 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 non-spangle galvanized sheet DX54D+Z from the 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 processes of steel smelting, hot rolling, cold rolling and continuous annealing, the advantages of low cost and good performance are achieved, and mechanical performance indexes of a finished product are as follows: yield strength is about 181 MPa, tensile strength is about 311 MPa, elongation rate is not less than 40%, n is about 0.22 and r value is not less than 2.20 or so.
Description
Technical field
The present invention relates to a kind of method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel, belong to the metallurgical plate production technical field.
Technical background
The definition of no zinc flower hot dip galvanized sheet DX54D+Z is: DX54D+Z is a kind of deep-draw galvanized sheet, is mainly used in the comparatively complicated part of punching press, Abdeckteil, and the DX54D+Z of this explained hereafter belongs to without zinc and spends surface, is characterized in that plate face zinc flower size is less than 1mm
2, erosion resistance, coating is better.At present production deep-draw rank galvanized sheet DX54D+Z is mainly used the IF steel, and in the IF steel, impurity is less, connects and moves 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%), the 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 formed 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.
Summary of the invention
The purpose of this invention is to provide a kind of method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel, do not add in addition microalloy element, improved the composition of conventional aluminum killed steel, C, Si content have been reduced, by improving steel-making, hot rolling, cold-rolling continuous annealing technique, 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:
A kind of method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel, comprise smelting, hot rolling, cold rolling, zinc-plated 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≤0.015%, S≤0.015%, Als:0.025～0.06%, N≤0.004%, remain as Fe.
In described smelting procedure, converter control is as follows: the mass ratio 10%/stove of the steel scrap of on average packing into, and 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 300 ± 10mm, provide 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 the converter molten steel Intake Quantity, in tapping process, every stove adds the aluminium slag of fluorite that mass percent is 0.009～0.0011%, 0.0020～0.0023% lime and 0.0014～0.0018% as top slag modifier.
In described smelting procedure, the RH vacuum processing time is calculated and is obtained by the mass transfer Equation Theory, and the treatment time is 20-33 minute, pure degassed 5-12 minute, final vacuum≤1.05mbar; Aluminum deoxidation after decarburization finishes, add high carbon ferromanganese to regulate manganese content; The assurance molten steel keeps molten steel calmness 30～60 minutes during opening to continuous casting after the RH processing finishes and watering, and the inclusion in the molten steel that fully floats, with pure molten steel.
Described hot-rolled process, require 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 630-710 ℃.
In e, course of hot rolling, the roughing stay-warm case normally drops into, and roughing is needless to say warm after finishing.
Described cold rolling process, acid is rolled draft and is controlled at 70～85%; Acid rolls into the product Roughness Surface on Control at 1.0～1.2 μ m.
In described zinc-plated operation, even moving back soaking temperature is 780～860 ℃, soaking time 80～200s; The slow cooling final cooling temperature is 640-700 ℃; Strip enters 455 ± 10 ℃ of zinc pot temperatures; The production belt speed is between 40～313m/min, and belt speed and thickness is coupling mutually; For eliminating the aluminium killed steel yield point elongation, the polishing unit elongation is set as 0.2-0.6%, and the straightening unit elongation is set as 0.1～0.4%, and polishing, straightening unit elongation arrange and must mutually mate with thickness.
In described zinc-plated operation, in described zinc-plated operation, zinc pot Al content is controlled at 0.18～0.23%, Pb≤30PPm, Sb≤20PPm, and zinc pot temperature is controlled at 460 ± 3 ℃.
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 improving steel-making, hot rolling, cold-rolling continuous annealing technique, 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, and performance is good, the finished product mechanical performance index: the about 191MPa of yield strength, the about 311MPa of tensile strength, unit elongation >=40%, n approximately 0.22, r value approximately >=2.20.
Embodiment
Below in conjunction with embodiment, further illustrate the present invention.
In an embodiment, comprise smelting, hot rolling, cold rolling, zinc-plated 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%)
The converter desulphurised hot metal of packing into is 270 tons.With respect to the converter molten steel Intake Quantity, in tapping process, every stove adds the aluminium slag of fluorite that mass percent is 0.00107%, 0.00214% lime and 0.0016% as top slag modifier.
Basicity of slag is controlled by 4.5, and the RH vacuum processing time is 26 minutes, and the pure degassed time is 10 minutes, final vacuum 1.00mbar.The RH vacuum processing technique calculates according to Mass Transfer Model.
Lower C content moves back by 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 40～120min, the finish rolling start rolling temperature is 1050 ± 10 ℃, 900 ± 10 ℃ of finishing temperatures, 700 ± 10 ℃ of coiling temperatures.
The embodiment trimmed size is two volume 1283 * 2.5mm.The 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 formed in the 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 the subsequent anneal process, is conducive to obtain thick ferritic structure.
3, cold rolling process: the acid of band steel rolls into the product specification and is 1250 * 0.5mm, and cold rolling draft is respectively 80%, and the finished product roughness is respectively 1. 2 ± 0.1 μ m.
4, zinc-plated operation
Concrete continuous annealing process is in Table 3.
Table 3 continuous annealing process
This is manufactured experimently smooth unit elongation and is set as 0.25%, and the straightening unit elongation is set as 0.1%.
C content is 0.01～0.02 o'clock, 730～770 ℃ of Ar1 temperature ranges.When soaking temperature is 800 ℃, 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, do not become mutually austenitic ferrite crystal grain grows up continuing in two-phase region, 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 descends, ferrite transformation will occur in the austenite of phase transformation, and oversaturated C will form Fe
3the C particle.Due to slow cooling section, in temperature-fall period, and the time is short, and the ferrite of phase transformation can't 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).When deformation occurs, thick ferrite is larger by grain-size, and C content is low, and precipitate is few, thereby reaches by surrender first occurs the effect that reduces yield strength.
The mechanical property of embodiment 1
Mechanical property is in Table 4.
Table 4 mechanical property
In table 4, mechanical property meets in GB GB/T2518-2008 fully about the relevant mechanical property requirements of DX54D+Z.
Claims (4)
1. a method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel, it is characterized in that comprising smelting, hot rolling, cold rolling, zinc-plated 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≤0.015%, S≤0.015%, Als:0.025～0.06%, N≤0.004%, remain as Fe; 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; Aluminum deoxidation after decarburization finishes, be not less than the lower limit requirement for guaranteeing C content, adds high carbon ferromanganese to regulate manganese content, carbon content;
C, assurance molten steel keep molten steel calmness 30～60 minutes during opening to continuous casting after the RH processing finishes and watering, and the inclusion in the molten steel that fully floats, with pure molten steel;
D, with respect to the converter molten steel Intake Quantity, in tapping process, every stove adds the aluminium slag of fluorite that mass percent is 0.009～0.0011%, 0.0020～0.0023% lime and 0.0014～0.0018% as top slag modifier.
2. a kind of method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel according to claim 1, is characterized in that described hot-rolled process, requires low-temperature heat, high-temperature final rolling, and 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 630-710 ℃;
In e, course of hot rolling, the roughing stay-warm case normally drops into, and roughing is needless to say warm after finishing.
3. a kind of described method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel according to claim 1 or 2, is characterized in that in described cold rolling process, and acid rolls into the product Roughness Surface on Control at 1.0～1.2 μ m.
4. a kind of described method of producing no zinc flower hot dip galvanized sheet DX54D+Z with aluminium killed steel according to claim 1 or 2 is characterized in that described zinc-plated operation:
A. connect that to move back soaking temperature be 780～860 ℃, soaking time 80～200s;
The slow cooling final cooling temperature is 640-700 ℃;
Strip enters 455 ± 10 ℃ of zinc pot temperatures;
The production belt speed is between 40～313m/min, and belt speed and thickness is coupling mutually;
B. the polishing unit elongation is set as 0.2-0.6%, and the straightening unit elongation is set as 0.1～0.4%, and polishing, straightening unit elongation must mate mutually with thickness;
C. zinc pot Al content is controlled at 0.18～0.23%, Pb≤30PPm, Sb≤20PPm, and zinc pot temperature is controlled at 460 ± 3 ℃.
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| CN104630614B (en) * | 2015-01-27 | 2017-02-22 | 唐山钢铁集团有限责任公司 | Method for improving forming performance of super-low-carbon aluminum killed steel galvanized product |
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| CN105256223A (en) * | 2015-11-12 | 2016-01-20 | 首钢总公司 | Micro-carbon steel with low yield strength and production method thereof |
| CN106756555A (en) * | 2016-12-19 | 2017-05-31 | 武汉钢铁股份有限公司 | Iron zinc coating steel plate and production method of a kind of yield strength for 160MPa grades |
| CN106521342A (en) * | 2016-12-19 | 2017-03-22 | 武汉钢铁股份有限公司 | Iron-zinc coated steel plate with yield strength being 130 MPa and production method thereof |
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| CN111647733B (en) * | 2020-05-11 | 2022-03-22 | 首钢集团有限公司 | Method for improving phosphating performance of low-carbon aluminum killed steel automobile plate and automobile plate |
| 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 |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999011835A1 (en) * | 1997-09-04 | 1999-03-11 | Kawasaki Steel Corporation | Steel plates for drum cans, method of manufacturing the same, and drum can |
| JP2980004B2 (en) * | 1995-08-07 | 1999-11-22 | 株式会社神戸製鋼所 | Cold rolled steel sheet excellent in burring workability and punching workability and its manufacturing method |
| WO1999063124A1 (en) * | 1998-05-29 | 1999-12-09 | Toyo Kohan Co., Ltd. | Resin-coated steel sheet suitable for use in thin-walled deep-drawn ironed can and steel sheet therefor |
| WO2007119665A1 (en) * | 2006-04-07 | 2007-10-25 | Nippon Steel Corporation | Process for producing alloyed hot-dip zinc-coated steel sheet satisfactory in processability, non-powdering property, and sliding property |
| CN101597674A (en) * | 2009-07-03 | 2009-12-09 | 首钢总公司 | A kind of continuous annealing method of DC 01 steel plate with low yield and high tensile strength for automobiles |
| CN101736195A (en) * | 2008-11-24 | 2010-06-16 | 攀钢集团研究院有限公司 | Hot-dip coating aluminium-zinc alloy steel plate and production method thereof |
| CN101812633A (en) * | 2009-02-23 | 2010-08-25 | 宝山钢铁股份有限公司 | Steel used for hot galvanizing structural component with high yield ratio and manufacturing method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5974237A (en) * | 1983-09-05 | 1984-04-26 | Sumitomo Metal Ind Ltd | Production of galvanized steel sheet for deep drawing having excellent formability |
| JPS5974236A (en) * | 1983-09-05 | 1984-04-26 | Sumitomo Metal Ind Ltd | Production of galvanized steel sheet for deep drawing having excellent formability |
-
2012
- 2012-06-19 CN CN 201210202941 patent/CN102758129B/en not_active Expired - Fee Related
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2980004B2 (en) * | 1995-08-07 | 1999-11-22 | 株式会社神戸製鋼所 | Cold rolled steel sheet excellent in burring workability and punching workability and its manufacturing method |
| WO1999011835A1 (en) * | 1997-09-04 | 1999-03-11 | Kawasaki Steel Corporation | Steel plates for drum cans, method of manufacturing the same, and drum can |
| WO1999063124A1 (en) * | 1998-05-29 | 1999-12-09 | Toyo Kohan Co., Ltd. | Resin-coated steel sheet suitable for use in thin-walled deep-drawn ironed can and steel sheet therefor |
| WO2007119665A1 (en) * | 2006-04-07 | 2007-10-25 | Nippon Steel Corporation | Process for producing alloyed hot-dip zinc-coated steel sheet satisfactory in processability, non-powdering property, and sliding property |
| CN101736195A (en) * | 2008-11-24 | 2010-06-16 | 攀钢集团研究院有限公司 | Hot-dip coating aluminium-zinc alloy steel plate and production method thereof |
| CN101812633A (en) * | 2009-02-23 | 2010-08-25 | 宝山钢铁股份有限公司 | Steel used for hot galvanizing structural component with high yield ratio and manufacturing method thereof |
| CN101597674A (en) * | 2009-07-03 | 2009-12-09 | 首钢总公司 | A kind of continuous annealing method of DC 01 steel plate with low yield and high tensile strength for automobiles |
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