CN103741031B - CSP is containing vanadium common orientation silicon steel and manufacture method thereof - Google Patents
CSP is containing vanadium common orientation silicon steel and manufacture method thereof Download PDFInfo
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Abstract
The present invention relates to a kind of based on continuous casting and rolling technique of sheet bar containing vanadium common orientation silicon steel and manufacture method thereof, belong to oriented electrical steel technical field.The chemical composition of thin slab is by mass percentage: C0.025 ~ 0.055%, Si2.5 ~ 4%, Mn0.05 ~ 0.2%, Cu0.4 ~ 0.6%, S0.005 ~ 0.01%, Al0.005 ~ 0.02%, N0.004 ~ 0.02%, P0.001 ~ 0.02%, V0.002 ~ 0.02%, all the other are Fe and inevitable impurity, and this oriented silicon steel is prepared as follows: sheet blank continuous casting → soaking pit heating → hot continuous rolling → first time is cold rolling → and decarburizing annealing → secondary cold-rolling → recovery annealing → painting MgO separant → high temperature annealing → cooling.The invention has the advantages that: adopt continuous casting and rolling technique of sheet bar, slab heating temperature is low, and soaking time is short, reduces energy consumption; Add proper amount of V and become auxiliary inhibitor, enhance rejection ability, improve finished product magnetic property.
Description
Technical field
The invention belongs to oriented electrical steel technical field.Particularly relate to a kind of CSP containing vanadium common orientation silicon steel and manufacture method thereof.
Background technology
In oriented silicon steel production process, in order to allow inhibitor element solid solution again separating out in course of hot rolling subsequently, thus obtain the inhibitor particle of a large amount of small and dispersed, strand heat is crucial.But heat brings immense pressure to aspects such as oriented silicon steel output, energy consumption, lumber recovery and equipment failures.Therefore, low temperature casting blank heating process progressively replaces conventional high-temperature heating process and becomes study hotspot in recent years.
At present, when traditional slab flow process adopts low temperature slab heating technique to produce common orientation silicon steel, slab heating temperature is generally at 1250 ~ 1300 DEG C.Adopt Cu
2s+AlN is inhibitor, and implements the secondary cold-rolling method of 60% ~ 70% medium draft, as Yi Xiete factory, Xin Lipeicike factory, Korea S's Pu item etc. in Russia.
In Russia, Yi Xiete metallurgical works adopts with Cu
2s is main, and AIN is auxiliary inhibitor.Strand composition is (wt%): C0.03 ~ 0.05, Mn0.2 ~ 0.25, Cu0.4 ~ 0.6, Als0.008 ~ 0.015, S0.017 ~ 0.02, N0.006 ~ 0.008, P<0.02.Xin Lipeicike steel metallurgical works adopts with Cu
2s and AlN is major inhibitors.Strand composition is (wt%): C0.03 ~ 0.05, Mn0.2 ~ 0.25, Cu0.4 ~ 0.6, Als0.013 ~ 0.02, S0.005 ~ 0.018, N0.007 ~ 0.009, P<0.02, Ni0.05, Cr0.05.Two factory's technological processs are: strand through 1250 ~ 1280 DEG C of hot rollings, 900 ~ 930 DEG C of finish to gauges; Secondary cold-rolling method is adopted to carry out cold rolling; Intermediate anneal temperature is 830 DEG C, at 5 wet ~ 10%H
2+ N
2decarburization is carried out in atmosphere.Wherein, second time cold rolling (draft is 55 ~ 65%) after at 10%H
2+ N
2, P
h2O/ P
h2the recovery annealing of 550 ~ 650 DEG C is carried out in=0.6 ~ 0.7 atmosphere; Be coated with MgO, carry out high temperature annealing (Li Shide, Niu Linxia, Russian electrical steel reduces costs technological measure analysis, electrical steel, 2(2000), pp.23-25).
Pohang Iron and Steel Corporation of Korea S is with Cu
2s and AIN is major inhibitors, its strand composition is (wt%): C0.035 ~ 0.05, Si2.9 ~ 3.3, Mn0.2 ~ 0.23, Cu0.4 ~ 0.5, P<0.015, Als0.011 ~ 0.017, N0.008 ~ 0.012, S<0.007, can 0.05Ni and/or 0.05Cr be added, and Mn/S>2.1, Cu/Mn>1.5.Technological process is: strand hot rolling after 1250 ~ 1320 DEG C × 3h heats; omit Hot Rolled Plate Normalizing, it is cold rolling to carry out first time, rolls and in 850 DEG C of wet protective atmospheres, carry out decarburizing annealing after 0.60 ~ 0.75mm; second time is cold-rolled to final thickness of slab 0.30mm, at wet protective atmosphere P
h2O/ P
h2carry out 600 ~ 750 DEG C × 45s ~ 2min recovery annealing in=0.62 ~ 0.88, being coated with MgO is main separant, is heated rapidly to 400 DEG C, with 20 ~ 50 DEG C/h heating rate to 700 DEG C, be heated to 1200 DEG C with 20 DEG C/h again, cool after soaking 20h, in 400 ~ 1200 DEG C of heat-processed, adopt 25%N
2+ 75%H
2protective atmosphere, the soaking stage adopts 100%H
2protective atmosphere (ChoiGS, MethodforManufacturingOrientedElectricalSteelbyHeatingSl abatlowTemperature [P] .US:5653821,1997).
When tradition slab flow process adopts low temperature slab heating technique to produce common orientation silicon steel, Cu
2s is usually used as main inhibitor, and AlN is as auxiliary inhibitor, and it is inadequate that it can make up the inhibitor rejection ability that sulfide suppressant causes because Solid solution precipitation is insufficient.In order to improve the rejection ability of inhibitor further, usually also can add other element and forming auxiliary inhibitor.As MnS, VN, TiN etc.VN was once proposed for the auxiliary inhibitor that traditional process produces high magnetic induction grain-oriented silicon steel before many years, to add the rejection ability of potent inhibitor, and improving product magnetic property.
Kawasaki, Japan once proposed, when taking MnSe+Sb+BN as inhibitor production high magnetic induction grain-oriented silicon steel, can add 0.01% ~ 0.02%V, form VN precipitated phase, make hot-rolled sheet and the refinement of decarburizing annealing plate recrystallized structure, and in final high-temperature annealing process, play the effect suppressing regular grain growth, to strengthen restraint to improve magnetic property (Zhang Ying, Fu Yunli, Wang Ruwu, inhibitor in high magnetic induction grain-oriented silicon steel, China is metallurgical, and (18) 2008, No.11, pp:4-8).
Nippon also once proposed when taking AlN+MnS+Sn as inhibitor production high magnetic induction grain-oriented silicon steel; 0.01% ~ 0.1%V can be added and form VN as auxiliary inhibitor to strengthen restraint; and 40 μm, decarburizing annealing rear surface region (110) pole density is improved; subgrain is tiny; final magnetic improves positive three youths of (Zhong Island; JiTomita Kang becomes; beautiful Trees is male for her rattan; magnetic mood characteristic Gifted れ height flux density one directivity Electricity magnetic Steel Ban System making method: Japan, clear 60-184632 [P] .1985.9.20; He Zhongzhi, Japan is electrical steel general situation of development in the recent period, electrical steel, (37) 1999, No.3, pp:2-5).
In order to reduce oriented silicon steel manufacturing cost further, compacter, more cheap production technique is all pursued by current all manufacturing factories.CSP is a kind of near net shape casting successfully developed late 1980s, through development for many years, has been tending towards ripe at present, will have had wide market outlook for the production of oriented silicon steel.Research shows, bar strip continuous casting and rolling flow path is adopted to produce oriented silicon steel short because having flow process, invest low, energy consumption is low, labour productivity high is subject to the most attention of Iron and Steel Production producer, wherein CSP is widely used a kind of technical process, after Thyssen utilizes CSP flow process production non orientating silicon steel for 1999 first, the CSP flow process that AST Iron And Steel Company of Italy builds up at Te Erni not only produced non orientating silicon steel, but also produced common orientation silicon steel and high magnetic induction grain-oriented silicon steel (GlovanniVespasiani, GiuseppeAbbruzzese:TechnologiesforTheProductionofElectri calStripatAcciaiSpeciali, Teni, TechnischeMitteilungenKrupp, 1 (1998), pp:42-48, FortunatiS, CIcaleS, AbbruzzeseG, ProcessfortheProductionofGrainOrientedElectricalSteelStr ipHavingHighMagneticCharacteristics, StartingfromThinSlab [P], US:6296719B1,2001, FortunatiS, CicaleS, AbbruzzeseG, ProcessfortheProductionofGrainOrientedElectricalSteelStr ipStartingfromThinSlab [P], US:6273964B1,2001).
Domestic less about adopting the research of continuous casting and rolling technique of sheet bar production common orientation silicon steel at present.Chinese patent application 200510047294.4,200710159088.1 and 200810229771.2 pairs of continuous casting and rolling technique of sheet bar are produced oriented silicon steel and have been done certain research, but their result of study otherwise magnetic property poor, be only about 30Q150 ~ 30Q140, slab heating temperature is higher, be greater than 1250 DEG C, and all do not add containing V inhibitor.Therefore, in the prior art, adopt the technology containing V common orientation silicon steel that CSP method processability is excellent, have not been reported so far.
Summary of the invention
The object of this invention is to provide a kind of CSP containing vanadium common orientation silicon steel and manufacture method thereof, reduce slab heating temperature and soaking time further, lower energy consumption, enhance productivity; Add appropriate V, form auxiliary inhibitor, strengthen rejection ability, improve finished product magnetic property.
The object of the invention is to be achieved through the following technical solutions:
A kind of CSP is containing vanadium common orientation silicon steel, the chemical composition of this thin slab is by mass percentage: C0.025 ~ 0.055%, Si2.5 ~ 4%, Mn0.05 ~ 0.2%, Cu0.4 ~ 0.6%, S0.005 ~ 0.015%, Als0.005 ~ 0.02%, N0.004 ~ 0.02%, P0.001 ~ 0.02%, V0.002 ~ 0.02%, and all the other are Fe and inevitable impurity;
This oriented silicon steel is prepared as follows: sheet blank continuous casting → soaking pit heating → hot continuous rolling → first time is cold rolling → and decarburizing annealing → secondary cold-rolling → recovery annealing → painting MgO separant → high temperature annealing → cooling.
This oriented silicon steel has following magnetic property, when the addition of V is 0.002 ~ 0.02%%, and magnetic strength B
800>=1.86T, iron loss P
17≤ 1.28w/kg.
Inhibitor is Cu
2s, AlN, MnS and VN, wherein, main inhibitor is Cu
2s, auxiliary inhibitor is AlN, MnS and VN.
CSP is containing the preparation method of vanadium common orientation silicon steel, the chemical composition of this thin slab is by mass percentage: C0.025 ~ 0.055%, Si2.5 ~ 4%, Mn0.05 ~ 0.2%, Cu0.4 ~ 0.6%, S0.005 ~ 0.015%, Als0.005 ~ 0.02%, N0.004 ~ 0.02%, P0.001 ~ 0.02%, V0.002 ~ 0.02%, and all the other are Fe and inevitable impurity;
Preparation method comprises the steps:
A. the slab that continuous casting obtains sends soaking pit soaking to without cooling direct hot charging heat, and soaking temperature is 1100 ~ 1200 DEG C, soaking 30 ~ 60 minutes;
B., after soaking, hot rolling and curling is carried out;
C. it is cold rolling to carry out first time;
D. through first time cold rolling laggard interline gross decarburization annealing;
E. secondary cold-rolling is carried out to finished product thickness 0.27mm;
F. the steel plate after secondary cold-rolling carries out recovery annealing;
G. recovery annealing plate is coated with MgO separant high temperature annealing obtains finished product.
The thickness of thin slab described in step a is 50mm.
In step b, start rolling temperature is 1100 ~ 1180 DEG C, and finishing temperature is 900 ~ 1000 DEG C, and hot-rolled sheet thickness is 2.2 ~ 2.4mm, and coiling temperature is 500 ~ 700 DEG C.
Described in step c, Cold Rolled Plate Thickness is 0.6 ~ 0.7mm for the first time.
Middle gross decarburization annealing described in steps d be first time cold rolling after steel plate within 5 ~ 10 minutes, carry out 850 ~ 900 DEG C of insulations.
Recovery annealing described in step f is that the steel plate after secondary cold-rolling carries out 500 ~ 700 DEG C of insulations for 2 ~ 8 minutes.
High-temperature annealing process described in step g, for be rapidly heated to 600 DEG C with stove, to be incubated 2 hours, to be heated to 1220 DEG C with 10 ~ 30 DEG C/h, and 1220 DEG C of insulations 8 ~ 12 hours, then cools.
High-purity H is adopted at 1220 DEG C of holding stages
2protective atmosphere; H is adopted in intensification and cooling stages
2+ N
2mixed gas protected atmosphere, wherein N
2shared volume percent is 20 ~ 60%.
CSP is containing the preparation method of vanadium common orientation silicon steel, and inhibitor is Cu
2s, AlN, MnS and VN, wherein, main inhibitor is Cu
2s, auxiliary inhibitor is AlN, MnS and VN.
Beneficial effect of the present invention is:
Compared with the present invention produces common orientation silicon steel technology with traditional slab flow process low temperature slab heating technique, not only reduce further the Heating temperature of slab to 1100 ~ 1200 DEG C, decrease the soaking time of strand by 30 ~ 60 minutes, and eliminate slab cooling and reheat process, shorten Production Flow Chart, greatly reduce energy consumption.In steel, add appropriate V, forming auxiliary inhibitor, providing enough restraints for forming stable secondary recrystallization, and the final magnetic property improving product.When interpolation 0.002 ~ 0.02, magnetic strength B
800>=1.86, iron loss P
1.7/50≤ 1.28W/kg, reaches 27Q130 standard completely.
Compared with traditional slab flow process, bar strip continuous casting and rolling flow path is produced oriented silicon steel and is had following technical superiority: Second Phase Precipitation thing is as Cu
2s, AlN, MnS and VN are more tiny, even, and the more effective inhibiting grain growth of energy, is conducive to the Fashion and Evolution of secondary recrystallization grain orientation texture, improves magnetic property; Microstructure and composition is even, and as-cast structure is good.Thin slab as-cast structure grain-size is tiny, and tissue and the composition difference of upper layer and central core are little; Slab heating temperature is low, the time is short, and the trouble that the strand heat of traditional technology can be avoided to bring also saves holding furnace, reduces technological process to a great extent, greatly reduces production cost; Trimming amount is little, and lumber recovery is high.Tradition thick stock technique is monolateral cuts 25mm, cuts 50mm altogether; Sheet bar process is monolateral cuts 10mm, cuts 20mm altogether; Capacity usage ratio is high.There is not the intercooling of strand-reheat process in continuous casting and rolling technique of sheet bar, strand heat can be made full use of, save energy, peach more holy than the energy-conservation 60%(enemy of traditional slab, Xiang Li, Yue Erbin, Zhao Pei, bar strip continuous casting and rolling flow path produces oriented silicon steel technical Analysis, iron and steel, (43) 2008, No.9, pp:1-6).
Embodiment
Below in conjunction with embodiment, the present invention is described in detail.
Chemical composition is as table 1, and all the other are Fe and inevitable impurity.
Embodiment 1
Processing step is as follows:
A. slab direct hot charging heat after continuous casting and solidifying sends soaking pit soaking to, and soaking temperature is 1180 DEG C.
B. soaking is after 30 minutes, carries out hot rolling.Start rolling temperature is 1150 DEG C, and finishing temperature is 900 DEG C, rolls into the hot-rolled sheet that 2.3mm is thick; Carry out curling at 550 DEG C.
C. it is cold rolling to carry out first time, and slab rolls 0.67mm.
D. through first time cold rolling laggard interline gross decarburization annealing, decarburizing annealing is carried out 875 DEG C of insulations for 8 minutes.
E. secondary cold-rolling is carried out to finished product thickness 0.27mm.
F. the steel plate after secondary cold-rolling carries out recovery annealing in 4 minutes 600 DEG C of insulations.
G. recovery annealing plate is coated with MgO separant.Finally carry out high temperature annealing.Wherein, the process of high temperature annealing, for being rapidly heated to 600 DEG C, being incubated 2 hours, being heated to 1220 DEG C with 20 DEG C/h, 1220 DEG C of insulations 8 hours, then cools.High-purity H is adopted at 1220 DEG C of holding stages
2protective atmosphere.H is adopted in intensification and cooling stages
2+ N
2mixed gas protected atmosphere, wherein N
2shared volume percent is 30%.Magnetic property measuring result is as shown in table 2.
Comparative example composition is as shown in table 1, for not adding V element or more V element in experimental steel composition.All the other techniques are identical with embodiment.
Table 1 experimental steel chemical composition (wt%)
| Embodiment | C | Si | Mn | Cu | S | Als | N | P | V |
| A | 0.036 | 3.13 | 0.08 | 0.52 | 0.0098 | 0.014 | 0.0083 | 0.01 | 0.002 |
| B | 0.035 | 2.55 | 0.12 | 0.48 | 0.0098 | 0.012 | 0.0086 | 0.01 | 0.002 |
| C | 0.042 | 3.13 | 0.05 | 0.5 | 0.015 | 0.013 | 0.012 | 0.01 | 0.008 |
| D | 0.055 | 3.95 | 0.13 | 0.59 | 0.012 | 0.005 | 0.013 | 0.02 | 0.008 |
| E | 0.043 | 3.1 | 0.09 | 0.4 | 0.008 | 0.016 | 0.004 | 0.001 | 0.019 |
| F | 0.026 | 2.9 | 0.2 | 0.46 | 0.005 | 0.02 | 0.019 | 0.006 | 0.02 |
| Comparative example 1 | 0.032 | 3.14 | 0.11 | 0.49 | 0.0096 | 0.015 | 0.0085 | 0.01 | 0.026 |
| Comparative example 2 | 0.037 | 3.15 | 0.1 | 0.51 | 0.0097 | 0.016 | 0.0084 | 0.01 | / |
Table 2 experimental steel magnetic property measuring result
| Numbering | P 17/50(w/kg) | B 800(T) |
| A1 | 1.26 | 1.87 |
| B1 | 1.27 | 1.88 |
| C1 | 1.18 | 1.89 |
| D1 | 1.17 | 1.90 |
| E1 | 1.22 | 1.87 |
| F1 | 1.23 | 1.88 |
| Comparative example 1-1 | 1.52 | 1.77 |
| Comparative example 1-2 | 1.31 | 1.81 |
Embodiment 2
Chemical composition is as shown in table 1, and all the other are Fe and inevitable impurity.
Processing step is as follows:
A. slab direct hot charging heat after continuous casting and solidifying sends soaking pit soaking to, and soaking temperature is 1100 DEG C.
B. soaking is after 45 minutes, carries out hot rolling.Start rolling temperature is 1100 DEG C, and finishing temperature is 950 DEG C, rolls into the hot-rolled sheet that 2.2mm is thick; Carry out curling at 500 DEG C.
C. it is cold rolling to carry out first time, and slab rolls 0.6mm.
D. through first time cold rolling laggard interline gross decarburization annealing, decarburizing annealing is carried out 850 DEG C of insulations for 5 minutes.
E. secondary cold-rolling is carried out to finished product thickness 0.27mm.
F. the steel plate after secondary cold-rolling carries out recovery annealing in 2 minutes 500 DEG C of insulations.
G. recovery annealing plate is coated with MgO separant.Finally carry out high temperature annealing.Wherein, the process of high temperature annealing, for being rapidly heated to 600 DEG C, being incubated 2 hours, being heated to 1220 DEG C with 10 DEG C/h, 1220 DEG C of insulations 10 hours, then cools.High-purity H is adopted at 1220 DEG C of holding stages
2protective atmosphere.H is adopted in intensification and cooling stages
2+ N
2mixed gas protected atmosphere, wherein N
2shared volume percent is 20%.Magnetic property measuring result is as shown in table 3.
Table 3 experimental steel magnetic property measuring result
| Numbering | P 17/50(w/kg) | B 800(T) |
| A2 | 1.28 | 1.88 |
| B2 | 1.26 | 1.87 |
| C2 | 1.17 | 1.90 |
| D2 | 1.16 | 1.90 |
| E2 | 1.21 | 1.86 |
| F2 | 1.24 | 1.87 |
| Comparative example 2-1 | 1.54 | 1.72 |
| Comparative example 2-2 | 1.3 | 1.82 |
Embodiment 3
Chemical composition is as shown in table 1, and all the other are Fe and inevitable impurity.
Processing step is as follows:
A. slab direct hot charging heat after continuous casting and solidifying sends soaking pit soaking to, and soaking temperature is 1200 DEG C.
B. soaking is after 60 minutes, carries out hot rolling.Start rolling temperature is 1180 DEG C, and finishing temperature is 1000 DEG C, rolls into the hot-rolled sheet that 2.4mm is thick; Carry out curling at 700 DEG C.
C. it is cold rolling to carry out first time, and slab rolls 0.7mm.
D. through first time cold rolling laggard interline gross decarburization annealing, decarburizing annealing is carried out 900 DEG C of insulations for 10 minutes.
E. secondary cold-rolling is carried out to finished product thickness 0.27mm.
F. the steel plate after secondary cold-rolling carries out recovery annealing in 8 minutes 700 DEG C of insulations.
G. recovery annealing plate is coated with MgO separant.Finally carry out high temperature annealing.Wherein, the process of high temperature annealing, for being rapidly heated to 600 DEG C, being incubated 2 hours, being heated to 1220 DEG C with 30 DEG C/h, 1220 DEG C of insulations 12 hours, then cools.High-purity H is adopted at 1220 DEG C of holding stages
2protective atmosphere.H is adopted in intensification and cooling stages
2+ N
2mixed gas protected atmosphere, wherein N
2shared volume percent is 60%.Magnetic property measuring result is as shown in table 4.
Table 4 experimental steel magnetic property measuring result
| Numbering | P 17/50(w/kg) | B 800(T) |
| A2 | 1.28 | 1.88 |
| B2 | 1.26 | 1.87 |
| C2 | 1.17 | 1.90 |
| D2 | 1.16 | 1.90 |
| E2 | 1.21 | 1.86 |
| F2 | 1.24 | 1.87 |
| Comparative example 3-1 | 1.54 | 1.72 |
| Comparative example 3-2 | 1.3 | 1.82 |
From table 2 ~ 4, Comparative Examples A, B, C, D, E, F and comparative example 1,2, can find out, add suitable V in steel, effectively can improve the magnetic strength B of common orientation silicon steel
800, reduce the iron loss P of common orientation silicon steel
17/50.Along with the increase of V content, magnetic property first improves gradually, rear reduction.As the excessive V(comparative example 1-2 of interpolation, 2-2,3-2) time, finished product magnetic property is poor, and it is unfavorable to produce oriented silicon steel.Major cause is start the increase along with V content, and rejection ability strengthens gradually, and therefore magnetic property improves gradually.As V too high levels (comparative example 1-1,2-1,3-1), not only can suppress the precipitation of AlN, also can form stable carbide, make finished product occur mixed crystal, cause finished product magnetic property to worsen.Therefore, only have and V content is controlled, in 0.002 ~ 0.02% scope, just can obtain the magnetic property of excellent property.
Claims (10)
1. a CSP is containing vanadium common orientation silicon steel, it is characterized in that, the chemical composition of this thin slab is by mass percentage: C0.025 ~ 0.055%, Si2.5 ~ 4%, Mn0.05 ~ 0.2%, Cu0.4 ~ 0.6%, S0.005 ~ 0.015%, Als0.005 ~ 0.02%, N0.004 ~ 0.02%, P0.001 ~ 0.02%, V0.002 ~ 0.02%, and all the other are Fe and inevitable impurity;
This oriented silicon steel is prepared as follows: sheet blank continuous casting → soaking pit heating → hot continuous rolling → first time is cold rolling → and decarburizing annealing → secondary cold-rolling → recovery annealing → painting MgO separant → high temperature annealing → cooling;
This oriented silicon steel has following magnetic property, when the addition of V is 0.002 ~ 0.02%, and magnetic strength B
800>=1.86T, iron loss P
17≤ 1.28W/kg.
2. as claimed in claim 1 containing vanadium common orientation silicon steel, it is characterized in that, inhibitor is Cu
2s, AlN, MnS and VN, wherein, main inhibitor is Cu
2s, auxiliary inhibitor is AlN, MnS and VN.
3. CSP as claimed in claim 1 is containing the preparation method of vanadium common orientation silicon steel, it is characterized in that, the chemical composition of this thin slab is by mass percentage: C0.025 ~ 0.055%, Si2.5 ~ 4%, Mn0.05 ~ 0.2%, Cu0.4 ~ 0.6%, S0.005 ~ 0.015%, Als0.005 ~ 0.02%, N0.004 ~ 0.02%, P0.001 ~ 0.02%, V0.002 ~ 0.02%, and all the other are Fe and inevitable impurity;
Preparation method comprises the steps:
A. the slab that continuous casting obtains sends soaking pit soaking to without cooling direct hot charging heat, and soaking temperature is 1100 ~ 1200 DEG C, soaking 30 ~ 60 minutes;
B., after soaking, hot rolling and curling is carried out;
C. it is cold rolling to carry out first time;
D. through first time cold rolling laggard interline gross decarburization annealing;
E. secondary cold-rolling is carried out to finished product thickness 0.27mm;
F. the steel plate after secondary cold-rolling carries out recovery annealing;
G. recovery annealing plate is coated with MgO separant high temperature annealing obtains finished product; Described high-temperature annealing process, for be rapidly heated to 600 DEG C with stove, to be incubated 2 hours, to be heated to 1220 DEG C with 10 ~ 30 DEG C/h, and 1220 DEG C of insulations 8 ~ 12 hours, then cools.
4. preparation method as claimed in claim 3, it is characterized in that, the thickness of thin slab described in step a is 50mm.
5. preparation method as claimed in claim 3, it is characterized in that, in step b, start rolling temperature is 1100 ~ 1180 DEG C, and finishing temperature is 900 ~ 1000 DEG C, and hot-rolled sheet thickness is 2.2 ~ 2.4mm, and coiling temperature is 500 ~ 700 DEG C.
6. preparation method as claimed in claim 3, is characterized in that, described in step c, Cold Rolled Plate Thickness is 0.6 ~ 0.7mm for the first time.
7. preparation method as claimed in claim 3, is characterized in that, middle the gross decarburization annealing described in steps d be cold rolling for the first time after steel plate within 5 ~ 10 minutes, carry out 850 ~ 900 DEG C of insulations.
8. preparation method as claimed in claim 3, it is characterized in that, the recovery annealing described in step f is that the steel plate after secondary cold-rolling carries out 500 ~ 700 DEG C of insulations for 2 ~ 8 minutes.
9. preparation method as claimed in claim 3, is characterized in that, adopt high-purity H at 1220 DEG C of holding stages
2protective atmosphere; H is adopted in intensification and cooling stages
2+ N
2mixed gas protected atmosphere, wherein N
2shared volume percent is 20 ~ 60%.
10. preparation method as claimed in claim 3, it is characterized in that, inhibitor is Cu
2s, AlN, MnS and VN, wherein, main inhibitor is Cu
2s, auxiliary inhibitor is AlN, MnS and VN.
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| CN109825775B (en) * | 2019-04-04 | 2020-03-27 | 中山市中圣金属板带科技有限公司 | Cold-rolled non-oriented electrical steel 35WD1900 and production method thereof |
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| CN101348851A (en) * | 2008-09-05 | 2009-01-21 | 首钢总公司 | Method for producing common oriented electrical steel by low temperature casting blank heating |
| CN102762752A (en) * | 2010-02-18 | 2012-10-31 | 新日本制铁株式会社 | Manufacturing method for grain-oriented electromagnetic steel sheet |
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