CN1796015A - Method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar - Google Patents
Method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar Download PDFInfo
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Abstract
The method for producing cold-rolled non-oriented electrical steel by using sheet bar and adopting continuous casting and continuous rolling process includes the following steps: a). utilizing the following components: C is less than or equal to 0.005%, Si is less than or equal to 3.5%, Mn is less than or equal to 1.5%, Al is less than or equal to 1.5%, P is less than or equal to 0.2%, S is less than or equal to 0.010%, N is less than or equal to 0.005%, O is less than or equal to 0.02% and the rest is iron and smelting; b). continuous casting, continuously casting molten steel to obtain sheet bar; c). heating, the temperature of sheet bar before which is fed into the furnace is 700-900deg.C, retaining said temperature for 30s-5min; heating sheet bar in ferrite phase area and heating temperature is less than or equal to 1120deg.C; d). hot-rolling, rolling in ferrite phase area, final rolling temperature is 800deg.C-950deg.C; e). coiling, coiling temperature is 500deg.C-900deg.C; and f). normalizing treatment or non-annealing treatment, acid-pickling, first cold-rolling or secondary cold-rolling with intermediate annealing to target thickness, then making final annealing so as to obtain the invented product.
Description
Technical field
The present invention relates to the manufacture method of non-oriented electrical steel, relate in particular to the method for the low cold rolling non-oriented electrical steel product of the good cost of CSP production magnetic.
Background technology
It is a kind of steel products that most steel plant use that line is produced in tradition continuous casting-hot rolling, the mode of production that comprises the cold rolling non-oriented electrical steel product, the pardon that is characterized in the production kind is fine, output big (a modern traditional hot rolling is produced the line annual production and can be reached 3,000,000 tons～4,000,000 tons).
It is to be that 0.8～1.5m/min, slab thickness are to carry out under the condition of 210mm～250mm at the continuous casting pulling rate that traditional continuous casting is produced non-orientation silicon steel.According to the design of this flow process, there is following problem for non-oriented electrical steel production:
Under common continuous casting degree of superheat condition (15 ℃～40 ℃), because pulling rate is very low, setting time is very long, the column crystal ratio reaches more than 80% usually for C content is lower than the electrical sheet of 50ppm and Si content 1.5%～2.5%, the ratio that is lower than 50ppm and silicone content column crystal greater than 2.5% non-orientation silicon steel for C content will reach 100%, and dendrite is thick, and production board produces serious corrugated defective, and the user can't use.Therefore the non-oriented electrical steel of high silicon content is set up electromagnetic mixing apparatus at continuous casting usually in the produced in conventional processes Ultra-low carbon, and the ratio of strand equiax crystal is brought up to more than 50%, thereby eliminates the corrugated defective.The production process complexity, the cost height.
Continuous casting adopts low overheat (＜15 ℃) also can improve the ratio of the non-oriented electrical steel equiax crystal of high silicon content in the Ultra-low carbon, but temperature treatment is very difficult between converter-refining-continuous casting, and molten steel is very low at mould temperature, viscosity increases, inclusion floating is very difficult, and the ratio of production board inclusion defects increases.Because the growing up of crystal grain when field trash hinders the production board final annealing makes the iron loss deterioration, field trash itself and stress field of forming around it also can hinder moving of neticdomain wall simultaneously, and form closure domain and produce demagnetizing field on every side at it, make the magnetic strength deterioration.Therefore no matter from organization of production, surface of steel plate still from magnetic property, the mode of taking the low overheat continuous casting all is worthless.
Take to improve the mode of molten steel C content,, when the non-orientation silicon steel continuous casting billet of high silicon content is in course of hot rolling in making a certain amount of phase transformation is arranged, in answer and recrystallization process, eliminate thick deformed grains as C being pressed 〉=[(Si+Al)-0.75] %/100 controls.Need dark decarburization when shortcoming is the production board final annealing, annealing time is multiplied, and annealing efficiency is very low, and influence connects the output of moving back the coating unit.This mode also is worthless.
The traditional hot rolling line of the general outfit of traditional continuous casting.Strand on the traditional hot rolling line when rolling the rolling line temperature fall bigger, the assurance ability of finishing temperature a little less than, the fluctuation of magnetic is very big.And often under low-temperature heat (as 1100 ℃), finishing temperature is lower, and improves very difficultly, and hot rolled plate percent crystallization in massecuite again is on the low side, and crystal grain is less, and magnetic is relatively poor.And the process of strand process cooling (generally being lower than 700 ℃)-again heating, strand heat energy fails to make full use of.
In recent years, the CSP production technology becomes new developing direction rapidly, compares production line with traditional production technology and can save 30% investment, saves the energy 30%～50%, the steel ton steel cost reduces by 200 yuan～360 yuan (China Metalurgy, in November, 2004).The slab thickness of CSP is generally 30～70mm, and the pulling rate when producing silicon steel is 2～8m/min.In this case, because pulling rate is very fast, the non-oriented electrical steel column crystal of middle high silicon content is tiny, and roll line length is short, temperature drop is little, finishing temperature control permission is bigger, compares with tradition product line and can obtain better hot rolled plate recrystallized structure, at the high grade non-oriented electrical steel product that does not have can obtain under the condition of electromagnetic agitation not having the corrugated defective.But it is thin that the problem that this technology exists is a strand, and cooling velocity is fast, strand charging temperature height (〉=900 ℃), cause MnS in the strand, AlN to have only on a small quantity and separate out, after finish to gauge, separate out in a large number going into the stokehold, particle is tiny, and grain growth was very unfavorable when production board was annealed, the iron loss deterioration.U.S. Pat 6503339 discloses and has adopted thin strand to obtain the precipitate of alligatoring from the method that is heated to austenite phase region, two-phase section hot rolling below 900 ℃, reaches the purpose of improving magnetic.Because slab heating temperature is higher, strand is cooled to the precipitates such as AlN of separating out below 900 ℃ may part solid solution again, finishes the back disperse in hot rolling subsequently and separates out, and grain growth is unfavorable during to final annealing.This patent has limited the content of Si and Al on the one hand, (Si+2Al≤3%), because Si, Al enlarge the ferrite element, on the other hand when producing the electrical sheet of higher Si, Al content (as Si 〉=2% or Si+2Al 〉=2%), for slab is heated in the austenitic area, must improve C content, then must decarburization when final annealing, one side production cost height (unit reduction of speed), magnetic bad (oxidation in easily producing) on the other hand.
Summary of the invention
The objective of the invention is to propose a kind of method of manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar product, magnetic is good, cost is low.
For achieving the above object, technical solution of the present invention is that the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar comprises the steps:
A. smelt by following composition: C≤0.005%, Si≤3.5%, Mn≤1.5%, Al≤1.5%, P≤0.2%, S≤0.01%, N≤0.005%, O≤0.02% and surplus iron more than are weight percentage;
B. continuous casting, molten steel becomes slab through continuous casting;
C. heating, it is 700 ℃～900 ℃ that slab is gone into the stokehold temperature, and keeps 30s～5min in this temperature; Strand is in ferrite phase region heating, heating-up temperature≤1120 ℃;
D. hot rolling, rolling at the ferrite phase region, 750 ℃～950 ℃ of finishing temperatures;
E. batch 500 ℃～900 ℃ of coiling temperatures;
F. normalizing is handled or unannealed processing, and pickling is then implemented final annealing after once cold rolling or the secondary cold-rolling that has intermediate annealing are rolled to target thickness, produces the non-oriented electrical steel product with this.
Further, add among Sn, Sb, Cu, Cr and the Ni one or more among the inventive method step a, the content range of individual element is for being no more than 0.2%.
Step b continuous casting pulling rate is 2～8m/min.
Step b continuous casting becomes the slab of 30～70mm thickness.
800 ℃～1100 ℃ of step f normalizing treatment temperatures.
The final cold rolling reduction ratio of step f is 30%～90%.
Principle of the present invention is described below:
Utilize the present invention on thin stock continuous casting hot rolling production equipment, can produce the non-oriented electrical steel product of low-cost and high-performance.Strand is gone into the stokehold and is stopped 30s～5min at 700 ℃～900 ℃, and heats and hot rolling≤1100 ℃ ferrite temperature province again, and MnS, AlN are separated out fully, and thickization, and production board grain growth inhibition is reduced.
The foundation that molten steel composition requires is:
Below the C:0.005%, C is the element that hinders grain growth strongly, causes that iron loss increases and magnetic aging, surpasses 0.005% and also will bring serious burden to decarburization.Preferably be controlled at below 0.003%.
Si:Si≤3.5%, Si are to increase the resistance element, are the most important alloying elements of electrical sheet, surpass 3.5% and will make electrical sheet processability deterioration, and magnetic strength reduces.
Mn：≤1.5％。Mn improves the electrical sheet surface state, reduces hot-short element, is higher than 1.5% and will makes steel plate processability deterioration.
Al：≤1.5％。Al increases the resistance element, is the most important alloying element of electrical sheet, and surpass 1.5% and will make smelting cast difficulty, steel plate processability deterioration, magnetic strength reduces.
P :≤0.2%, in steel, add the processability that certain phosphorus can improve steel plate, make steel plate cold-workability deterioration on the contrary but surpass at 0.2% o'clock.
Below the S:0.01%, surpass 0.01% the Sization thing amount of separating out such as MnS will be increased greatly, hinder grain growth strongly, the iron loss deterioration.
Below the N:0.005%, surpass 0.005% the Nization thing amount of separating out such as AlN will be increased greatly, hinder grain growth strongly, the iron loss deterioration.
Below the O:0.02%, surpass 0.02% the oxide inclusion amount will be increased greatly, hinder grain growth strongly, make simultaneously to be mingled with the demagnetizing field increase that causes, iron loss and magnetic strength deterioration.
Can add among a certain amount of Sn, Sb, Cu, Cr and the Ni one or more to improve the texture of production board, magnetic strength is improved, but the content range of individual element makes the magnetic reduction on the contrary for being no more than 0.2%.
The molten steel of mentioned component becomes the slab of 30～70mm thickness through the casting speed continuous casting of 2～8m/min, slab go into the stokehold 900 ℃ to the temperature range retention time more than 700 ℃ be 30s～5min, to guarantee that AlN can fully separate out, after this slab enters the heating furnace heating immediately.In heating furnace, strand is in ferrite phase region heating, and maximum temperature≤1120 ℃, under this temperature heating the AlN, the MnS that separate out are before this assembled grow up, alligatoring, reduce inhibition to grain growth.Be hot-rolled down to 1.0～3.0mm then, 800 ℃～950 ℃ of finishing temperatures, 500～900 ℃ of coiling temperatures.This hot rolling band is implemented 800 ℃～1100 ℃ annealing or unannealed processing, and pickling is after once cold rolling or the secondary cold-rolling that has intermediate annealing are rolled to target thickness, and final cold rolling reduction ratio is 30%～90%, then implements final annealing.With this non-oriented electrical steel product that production magnetic is good and cost is low.
The invention has the advantages that the temperature that the control continuous casting steel billet is gone into the stokehold, under this temperature, keep plenty of time that AlN is fully separated out simultaneously, and in follow-up ferrite phase region (≤1120 ℃) heating process, can assemble grow up, alligatoring, avoided the problem that the AlN small and dispersed is separated out after the hot rolling finish to gauge that previous methods causes.Crystal grain is easily grown up in the time of can obtaining the cold-reduced sheet final annealing with this, the product that iron loss is lower.
The specific embodiment
Method of the present invention is:
Molten steel becomes the slab of 30～70mm thickness through the casting speed continuous casting of 2～8m/min, and it is 700 ℃～900 ℃ that slab is gone into the stokehold temperature, and keeps 30s～5min in this temperature, and after this slab enters the heating furnace heating immediately.In heating furnace, strand is in ferrite phase region heating, and maximum temperature≤1120 ℃, is hot-rolled down to 1.0～3.0mm then, 750 ℃～950 ℃ of finishing temperatures, 500～900 ℃ of coiling temperatures.This hot rolling band is implemented 800 ℃～1100 ℃ annealing or unannealed processing, and pickling is after once cold rolling or the secondary cold-rolling that has intermediate annealing are rolled to target thickness, and final cold rolling reduction ratio is 30%～90%, then implements final annealing.With this non-oriented electrical steel product that production magnetic is good and cost is low;
Embodiment 1:
Converter, RH application of vacuum obtain C:0.0015%, Si:0.25%, Mn:1.5%, Al:0.50%, P:0.08%, S:0.005%, N:0.0020%, O:0.0015%, Sb 0.05%, surplus is the molten steel of Fe, makes the thin stock of 50mm under the pulling rate of 6m/min through continuous casting, heating and hot rolling again shown in the table 1.The hot rolling reeling temperature is 700 ℃.After this hot rolled plate pickling, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm, as shown in table 1 through the magnetic that final annealing obtains.The phase transition temperature Ac1 of this composition strand is 1060 ℃.
Table 1
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 11 | 0.8 | 1050 | 900 | 2.30 | 4.80 | 1.78 |
| Embodiment 12 | 3 | 1000 | 880 | 2.30 | 4.60 | 1.78 |
| Comparative example 11 | (1000 ℃ of charging temperatures) | 1100 | 830 | 2.30 | 6.50 | 1.74 |
| Comparative example 12 | 1 | 1180 | 870 | 2.30 | 6.00 | 1.75 |
Wherein, embodiment 11,12 is the result under the process conditions of the present invention, and comparative example 11,12 is for exceeding the result under the process conditions of the present invention.Therefrom as can be seen, magnetic of the present invention is more superior than prior art.
Embodiment 2:
Converter, RH application of vacuum obtain C:0.0020%, Si:1.10%, Mn:0.25%, Al:0.25%, P:0.008%, S:0.004%, N:0.0015%, O:0.0015%, surplus is the molten steel of Fe, under the pulling rate of 4m/min, make the thin stock of 45mm, implement heating and hot rolling again shown in the table 2 through continuous casting.The hot rolling reeling temperature is 800 ℃, implements self annealing.After this hot rolled plate pickling, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm, as shown in table 2 through the magnetic that final annealing obtains.The phase transition temperature Ac1 of this composition strand is 1105 ℃.
Table 2
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 21 | 1 | 1010 | 900 | 1.80 | 4.00 | 1.75 |
| Embodiment 22 | 5 | 980 | 850 | 2.10 | 3.90 | 1.75 |
| Comparative example 21 | (1000 ℃ of charging temperatures) | 1100 | 830 | 2.10 | 4.80 | 1.74 |
| Comparative example 22 | 3 | 1200 | 870 | 2.10 | 5.50 | 1.73 |
According to the method for US6053339, the invention member condition is Si:1.3%, Mn:0.20%, Al:0.12%, and is close with mentioned component in addition.The magnetic of not implementing final thickness that normalizing obtains and be the 0.5mm plate is P
15/50: 4.5W/kg, magnetic strength B
25Be 1.668T (B50 is about 1.75T).Magnetic is obviously than the present invention difference.
Embodiment 3:
Converter, RH application of vacuum obtain C:0.0020%, Si:2.10%, Mn:0.20%, Al:0.30%, P:0.008%, S:0.004%, N:0.005%, O:0.0015%, surplus is the molten steel of Fe, under the pulling rate of 3m/min, make the thin stock of 45mm, implement heating and hot rolling again shown in the table 3 through continuous casting.The hot rolling reeling temperature is 800 ℃, implements self annealing.After this hot rolled plate pickling, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm, as shown in table 3 through the magnetic that final annealing obtains.This composition strand does not have transformation temperature.
Table 3
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 31 | 1 | 1100 | 900 | 2.10 | 3.20 | 1.74 |
| Embodiment 32 | 4 | 1050 | 850 | 2.10 | 2.90 | 1.73 |
| Comparative example 31 | (1000 ℃ of charging temperatures) | 1100 | 830 | 2.10 | 3.80 | 1.70 |
| Comparative example 32 | 3 | 1200 | 870 | 2.10 | 4.00 | 1.70 |
According to the method for US6053339, the invention member condition is Si:1.8%, Mn:0.20%, Al:0.35%, and is close with mentioned component in addition.The magnetic of not implementing final thickness that normalizing obtains and be the 0.5mm plate is P
15/50: 4.02W/kg, magnetic strength B
25Be 1.617T (B50 is about 1.70T).Magnetic is obviously than the present invention difference.
Embodiment 4:
Converter, RH application of vacuum obtain C:0.005%, Si:3.0%, Mn:0.25%, Al:0.8%, P:0.010%, S:0.0025%, N:0.0015%, O:0.0015%, surplus is the molten steel of Fe, make the thin stock of 30mm through continuous casting under the pulling rate of 2m/min, implement heating and hot rolling again shown in the table 4, the hot rolling reeling temperature is 550 ℃.After this hot rolled plate carries out 950 ℃ * 2min annealing, and pickling then, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm are as shown in table 4 through the magnetic that final annealing obtains.This composition strand does not have transformation temperature.
Table 4
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 41 | 0.5 | 1120 | 950 | 1.80 | 2.30 | 1.70 |
| Embodiment 42 | 4 | 1050 | 900 | 1.80 | 2.20 | 1.70 |
| Comparative example 41 | (1000 ℃ of charging temperatures) | 1100 | 830 | 1.80 | 2.80 | 1.68 |
| Comparative example 42 | 2 | 1150 | 870 | 1.80 | 3.20 | 1.68 |
Embodiment 5:
Converter, RH application of vacuum obtain C:0.003%, Si:3.30%, Mn:0.25%, Al:1.5%, P:0.010%, S:0.0025%, N:0.0015%, O:0.0015%, surplus is the molten steel of Fe, make the thin stock of 30mm through continuous casting under the pulling rate of 2m/min, implement heating and hot rolling again shown in the table 4, the hot rolling reeling temperature is 550 ℃.After this hot rolled plate carries out 950 ℃ * 2min annealing, and pickling then, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm are as shown in table 5 through the magnetic that final annealing obtains.This composition strand does not have transformation temperature.
Table 5
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 51 | 0.5 | 1120 | 950 | 1.80 | 2.00 | 1.69 |
| Embodiment 52 | 4 | 1050 | 900 | 1.80 | 1.90 | 1.69 |
| Comparative example 51 | (1000 ℃ of charging temperatures) | 1100 | 830 | 1.80 | 2.50 | 1.67 |
| Comparative example 52 | 2 | 1180 | 870 | 1.80 | 2.90 | 1.67 |
Embodiment 6:
Converter, RH application of vacuum obtain C:0.0020%, Si:1.10%, Mn:0.25%, Al:0.001%, P:0.02%, S:0.004%, N:0.002%, O:0.015%, surplus is the molten steel of Fe, under the pulling rate of 4m/min, make the thin stock of 45mm, implement heating and hot rolling again shown in the table 2 through continuous casting.The hot rolling reeling temperature is 800 ℃, implements self annealing.After this hot rolled plate pickling, the thick cold-reduced sheet of cold rolling one-tenth 0.50mm, as shown in table 6 through the magnetic that final annealing obtains.The phase transition temperature Ac1 of this composition strand is 1010 ℃.
Table 6
| Sequence number | Slab is in 700 ℃～900 ℃ following retention times (min) | Strand heating ℃ | Finishing temperature ℃ | Hot rolled plate thickness mm | P 15/50 W/kg | B 50 T |
| Embodiment 61 | 1 | 1010 | 900 | 1.80 | 4.50 | 1.75 |
| Embodiment 62 | 5 | 980 | 850 | 2.10 | 4.40 | 1.75 |
| Comparative example 61 | (1000 ℃ of charging temperatures) | 1100 | 830 | 2.10 | 4.80 | 1.74 |
| Comparative example 62 | 3 | 1200 | 870 | 2.10 | 5.50 | 1.73 |
From table 1～table 6 as can be seen, the magnetic of the non-oriented electrical steel of manufacturing of the present invention, iron loss, magnetic induction performance all are better than existing non-oriented electrical steel with the continuous casting and rolling technique of sheet bar manufacturing.
Claims (6)
1. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar comprises the steps:
A. smelt by following composition: C≤0.005%, Si≤3.5%, Mn≤1.5%, Al≤1.5%, P≤0.2%, S≤0.01%, N≤0.005%, O≤0.02% and surplus iron more than are weight percentage;
B. continuous casting, molten steel becomes slab through continuous casting;
C. heating, it is 700 ℃～900 ℃ that slab is gone into the stokehold temperature, and keeps 30s～5min in this temperature; Strand is in ferrite phase region heating, heating-up temperature≤1120 ℃;
D. hot rolling, rolling at the ferrite phase region, 750 ℃～950 ℃ of finishing temperatures;
E. batch 500 ℃～900 ℃ of coiling temperatures;
F. normalizing is handled or unannealed processing, and pickling is then implemented final annealing after once cold rolling or the secondary cold-rolling that has intermediate annealing are rolled to target thickness, produces the non-oriented electrical steel product with this.
2. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar as claimed in claim 1 is characterized in that, adds among Sn, Sb, Cu, Cr and the Ni one or more among the step a, and the content range of individual element is for being no more than 0.2%.
3. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar as claimed in claim 1 is characterized in that, step b continuous casting pulling rate is 2～8m/min.
4. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar as claimed in claim 1 is characterized in that, step b continuous casting becomes the slab of 30～70mm thickness.
5. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar as claimed in claim 1 is characterized in that, 800 ℃～1100 ℃ of step f normalizing treatment temperatures.
6. the method for manufacturing cold rolling non oriented electrical steel through continuous casting and tandem rolling sheet bar as claimed in claim 1 is characterized in that, the final cold rolling reduction ratio of step f is 30%～90%.
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