CN108018489A - A kind of economical high magnetic induction grain-oriented silicon steel and production method - Google Patents

A kind of economical high magnetic induction grain-oriented silicon steel and production method Download PDF

Info

Publication number
CN108018489A
CN108018489A CN201711354380.9A CN201711354380A CN108018489A CN 108018489 A CN108018489 A CN 108018489A CN 201711354380 A CN201711354380 A CN 201711354380A CN 108018489 A CN108018489 A CN 108018489A
Authority
CN
China
Prior art keywords
temperature
annealing
magnetic induction
silicon steel
oriented silicon
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CN201711354380.9A
Other languages
Chinese (zh)
Inventor
杨佳欣
申明辉
郭小龙
胡守天
骆忠汉
高洋
骆新根
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Wuhan Iron and Steel Co Ltd
Original Assignee
Wuhan Iron and Steel Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Wuhan Iron and Steel Co Ltd filed Critical Wuhan Iron and Steel Co Ltd
Priority to CN201711354380.9A priority Critical patent/CN108018489A/en
Publication of CN108018489A publication Critical patent/CN108018489A/en
Pending legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D3/00—Diffusion processes for extraction of non-metals; Furnaces therefor
    • C21D3/02—Extraction of non-metals
    • C21D3/04—Decarburising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

A kind of economical high magnetic induction grain-oriented silicon steel, its component and wt% are：C：0.015~0.095%, Si：2.80~3.60%, Als：0.010~0.015%, N：0.0050~0.0100%, Mn：0.010~1.00%, S：0.0030~0.0150%, Bi：0.0015~0.100% you, the sum of P, Cu, Sn, Sb, Cr and As be no more than 0.80%；Production method：Smelt and be casting continuously to form base；To heating strand；Carry out segmentation hot rolling；Batch；Normalizing；Disposable cold rolling is carried out after pickling；Decarburizing annealing；It is coated with high annealing interleaving agent；Carry out the high annealing with secondary insulation；Stretching and leveling and coating insulating coating.The present invention can obtain steel plate magnetic induction density B 800 and be not less than 1.930T, iron loss P17/50≤1.08W/k, magnetic property is stablized, and cost can be dropped not less than 5% relative to the prior art under the conditions of without nitriding.

Description

A kind of economical high magnetic induction grain-oriented silicon steel and production method
Technical field
The present invention relates to a kind of orientation silicon steel and production method, particularly belongs to a kind of high magnetic induction grain-oriented silicon steel and producer Method.
Background technology
At present, according to the difference of inhibitor system, industrial production high temperature heating strand orientation silicon steel have three kinds it is representational Technology, it is magnetic can all to obtain higher finished product.But many problems can be produced in 1400 DEG C of high-temperature heating strand, such as aoxidize Slag increases, scaling loss is big, lumber recovery reduces, it is high to repair stove frequency, manufacture cost increases, surface defects of products is more etc..Using relatively low Slab heating temperature then can effectively avoid these problems, while can also reduce the energy consumption cost in production.Use low temperature at present （Heating-up temperature≤1280 DEG C）The orientation silicon steel industrial production of heating of plate blank mainly has：1）Using the Russian of intrinsic inhibitor （AlN+Cu）Component system；2）Use that the later stage obtains inhibitor is representative after hot rolling to before high annealing using nippon Nitridation process；3）The production technology by High Purity no inhibitor of JFE exploitations.It is Russian in aforementioned production method（AlN+ Cu）It is technique, the Cu that there is amount to be added（0.50%）, and produced using secondary cold-rolling method, it is of high cost, and surface quality is difficult to Control, performance B8＜ 1.89T；Nippon Steel's technique need to increase Nitrizing Treatment before high annealing；And the no inhibitor technique of JFE is then It is required that steel high purification（The ＜ 30ppm such as S, N, O, Als）, add steel-making cost.
Again through retrieval：Chinese patent literature number is the document of CN201110444436.6, discloses one kind sheet billet The general orientation silicon steel and manufacture its method that continuous casting and rolling produces.Its component and percentage by weight are：C：0.015~0.055%, Si：2.5~4.0%, Mn：0.10~0.40%, P≤0.025t%, S≤0.010%, Als：0.010~0.025%, N： 0.0065~0.0075%, Cu：0.30~0.60%, remaining is Fe and inevitable impurity；Its step：Smelt and use thin Slab continuous casting rolling；First time cold rolling after pickling；Containing moist N2、H2Gross decarburization annealing among being carried out under atmosphere；Second Secondary cold rolling, is rolled to required thickness；In N2、H2Carried out under atmosphere recovery annealing, coating magnesia interleaving agent, carry out high annealing, into The smooth stretching of row, and apply layer of cloth.The document reduces the solid solubility temperature of inhibitor by the use of AlN and ε-Cu as inhibitor, and Process is not required to normalizing, nitriding afterwards, and production cost reduces, and end properties are uniform.Although it is not required to carry out Nitrizing Treatment, need to adopt With secondary cold-rolling, production lumber recovery is reduced, adds production cost.And its magnetic strength is less than 1.89T, the effect of high magnetic strength is not up to Fruit.
Chinese Patent Application No. is the document of CN201210461025.2, discloses a kind of high magnetic induction grain-oriented silicon steel and its life Production method, its chemical component weight percentage are：C 0.035~0.120%, Si 2.5~4.5%, Mn 0.05~0.20%, S 0.005~0.050%, Als 0.015~0.035%, N 0.003~0.010%, Sn 0.03~0.30%, Cu 0.01~ More than one in 0.50%, V≤0.0100%, Ti≤0.0100%, Sb, Bi, Ni and Mo, remaining for Fe and it is other inevitably Impurity；Its step：Smelt, after casting, 1200~1330 DEG C of slab heating temperature, 150~600min of heating time, conventional hot rolling Afterwards, normalizing annealing is carried out to hot rolled coil, is cooled down after normalizing annealing, 10~100 DEG C/sec of cooling velocity, is cold rolled to production board Thickness, cold rolling reduction ratio >=85%, programming rate, decarburizing atmosphere and decarburization dew point are routinely set, decarburization temperature 800~900 DEG C, 80~160sec of time, or Nitrizing Treatment is carried out after decarburizing annealing, penetrate into 50~260ppm of nitrogen content, the heating temperature of strand 1050~1150 DEG C of degree, carries out MgO coatings to the steel plate of above-mentioned decarburizing annealing and is carried out in bell furnace or annular furnace conventional high Temperature annealing, insulating coating is applied in high annealing plate surface, and the high magnetic strength for obtaining excellent magnetic through the smooth annealing of hot-stretch takes To silicon steel.The invention is using medium temperature hot rolling or Low Temperature Hot Rolling and Nitrizing Treatment, using once rolling, slab heating temperature or 1200 ~1330 DEG C, or 1050~1150 DEG C but Nitrizing Treatment is needed, equally add production cost.
Chinese Patent Application No. is the document of CN201310666117.9, discloses a kind of high magnetic induction grain-oriented silicon steel and its life Production method, its chemical component weight percentage are：C 0.055~0.095%, Si 2.95~3.25%, Mn 0.050~ 0.090%, P≤0.01%, S 0.010~0.025%, N 0.006~0.010%, Cr 0.05~0.5%, Als 0.020~ 0.030%, Bi 0.002~0.1%, Se 0.01~0.06%, Sb 0.01~0.06%, remaining for Fe and it is other inevitably Impurity；Production stage：By heating strand, hot rolling, normalizing treatment, using once cold rolling method or the secondary cold-rolling method containing intermediate annealing Pair rolling is to finished product thickness, and decarburizing annealing, is coated with the interleaving agent using magnesia as main component, using the high temperature of secondary insulation Annealing, stretching and smooth annealing, layer of cloth is applied in surface of steel plate；The present invention by individually add or it is compound addition Sb, Se and Bi crystal boundary segregation elements, improve orientation silicon steel magnetic induction intensity, and B800 is not less than 1.95T, and magnetic stability.The present invention uses High temperature hot rolling, using once cold rolling method or the secondary cold-rolling method containing intermediate annealing, can stablize and obtain B800 taking not less than 1.95T To silicon steel finished product, but the present invention is reduced lumber recovery, is added production cost using 1320~1400 DEG C of high-temperature heating hot rollings. And lumber recovery can be reduced.
The content of the invention
It is an object of the invention to overcome the shortcomings of the prior art, there is provided a kind of condition without nitriding process Under, its finished steel plate magnetic induction density B 800 is not less than 1.93T, and iron loss P17/50≤1.08W/k, cost is relative to existing skill Economical high magnetic induction grain-oriented silicon steel and production method not less than 5% can drop in art.
Realize the measure of above-mentioned purpose：
A kind of economical high magnetic induction grain-oriented silicon steel, its component and weight percent content are：C：0.015~0.095%, Si：2.80 ~3.60%, Als：0.010~0.015%, N：0.0050~0.0100%, Mn：0.010~1.00%, S：0.0030~ 0.0150%, Bi：0.0015~0.100%, one or both of addition P, Cu, Sn, Sb, Cr and As the compound of the above add Add, and meet that the sum of P, Cu, Sn, Sb, Cr and As are no more than 0.80%, remaining is iron and inevitable impurity.
Preferably： N：0.005%~0.0095%, Mn：0.018%~0.93%, S：0.0030%~0.010%, Bi： 0.002%~0.09%.
Produce a kind of method of economical high magnetic induction grain-oriented silicon steel, its step：
1）Routine smelts, is casting continuously to form base；
2）To heating strand, heating and temperature control is at 1150 ~ 1200 DEG C；
3）Segmentation carries out hot rolling, and it is 2.0~2.5mm to be rolled to thickness, and controls finishing temperature at 850 DEG C~1000 DEG C；
4）Batched, coiling temperature is no more than 600 DEG C；
5）Normalizing is carried out, normalizing temperature keeps the temperature 30~180s at this temperature at 1000 DEG C~1150 DEG C；
6）Disposable cold rolling is carried out after conventional pickling, and controlled rolling reduction ratio is not less than 90%；
7）Carry out decarburizing annealing, decarburization annealing temperature at 750~900 DEG C, soaking time in 60~180s, dew point at 23 ~ 27 DEG C, Protective atmosphere is H2And N2Wet mixed gas, wherein H2Volume content is 15~80%；
8）It is coated with the high annealing interleaving agent using MgO as main component；
9）Carry out the high annealing with secondary insulation：When annealing temperature rises to 800~1120 DEG C, first time insulation is carried out, Soaking time is in 5~22 hours；In this annealing stage, annealing atmosphere is pure nitrogen gas or the mixed gas of nitrogen and hydrogen, is mixed Close the percent by volume that hydrogen accounts in gas and be no more than 50%；Therebetween, from when being warming up to 1100 DEG C for 850 DEG C, control rises annealing temperature Warm speed is at 5~60 DEG C/h；
When annealing temperature rises to 1150~1230 DEG C, carry out second and keep the temperature, soaking time is in 5~30 hours, and complete Carried out under nitrogen atmosphere；
10）Carry out stretching and leveling and coating insulating coating.
Preferably：Slab heating temperature is at 1100 ~ 1185 DEG C.
Preferably：Step 9）When middle progress is annealed for the first time, during annealing temperature is warming up to 1050 DEG C from 850 DEG C, control Programming rate processed is at 12~55 DEG C/h.
Preferably：Step 9）Middle first time annealing temperature is at 845~1095 DEG C.
Preferably：Step 9）In second of annealing temperature at 1150~1210 DEG C.
Each component and main technique effect and mechanism in the present invention
C, carbon be orientation silicon steel manufacture important element, C be less than 0.03% when, especially less than 0.02% when 3.25%Si steel Without phase-change, crystal grain is substantially roughened strand when heated, deformation coarse grains of the hot-rolled strip along thickness of slab direction center,<110>It is fine Dimension texture is strong, the tangible change crystal grain of remaining after cold rolling and decarburizing annealing, and secondary recrystallization is incomplete after high annealing, makes magnetic drop It is low, but carbon content is excessive, and decarburization can be caused difficult, and therefore, carbon content is 0.015%~0.095%.
Si, Si is added in oriented electrical steel can increase resistivity, reduce iron loss, but the increase of Si contents can cause to process Brittleness, therefore, to ensure that processability need to control the content of Si, Si contents are between 2.80%~3.60%.
Mn, S, in the high temperature orientation silicon steel production of the heating at >=1360 DEG C, Mn, S separate out MnS formation elements to be favourable, because This S >=0.0250%, but the present invention emphasizes 1150 DEG C~1200 DEG C Low Temperature Hot Rollings, and using AlN and Bi as major inhibitors, and Mn Content, which improves, can reduce eddy-current loss, thus control Mn contents 0.010%~1.00%, S contents 0.0030%~ 0.0150%；Preferably：Mn is in 0.018~0.93%, S 0.0030~0.010%.
Als, N, separate out AlN formation elements, the present invention emphasizes 1150 DEG C~1200 DEG C Low Temperature Hot Rollings, therefore Als to be favourable In 0.010%~0.015%, N 0.0050%~0.0100%.
Bi is interface enriched element, because its atomic radius is larger, it is extremely difficult to rich easily in phase boundary, crystal boundary in transgranular solid solution Collection, so as to prevent growing up for the second phase and matrix grain, the present invention is using AlN and Bi as major inhibitors, but Bi too high levels are easy Cause hot-rolling edge cracking big and surface quality in kind is poor, therefore Bi is in 0.0015%~0.100%, preferably Bi：0.002%~ 0.09%.
P, Cu, Sn, Sb, Cr and As, to supplement inhibitor formation element, its total content≤0.80%.
Why the present invention controls the heating-up temperature of strand at 1150 ~ 1200 DEG C, is due to when heating-up temperature is less than 1150 DEG C when slab in the precipitate such as AlN be difficult to be dissolved, heating-up temperature can cause slab grain coarsening higher than 1200 DEG C, and energy consumption increases Add.Preferably slab heating temperature is at 1100 ~ 1185 DEG C
The present invention why finishing temperature is limited in the range of 850~1000 DEG C, with ensure in the range of higher warm area into Row hot rolling, and higher finishing temperature, do not separate out the Second Phase Particles such as the AlN of bulky grain in the hot rolling.
Why the present invention 1000 DEG C~1150 DEG C at a temperature of keeps the temperature 30~180s to Hot Rolled Plate Normalizing, to ensure The suitable AlN Second Phase Particles of size complete solid solution, and when cooling forms the second favourable phase.At a temperature of less than 1000 DEG C into Row normalizing, since temperature is low, AlN is difficult to be dissolved；Higher than 1150 DEG C steel band grain coarsenings, cause crystal grain after primary recrystallization annealing Grow up, while increase cost.
Why the present invention controls decarburization annealing temperature at 750~900 DEG C, keeps the temperature 60~180s, and dew point is 25 DEG C, protection Atmosphere is wet H2And N2Mixed gas, H2Volume content：15~80%, it is therefore an objective to：Primary recrystallization is completed, makes to have in matrix Sufficient amount of [110] (001) crystal grain（Secondary nucleus）And be conducive to primary recrystallization tissue and texture that they grow up；Will Carbon is taken off to less than 0.0030% in steel, and high annealing is in single α phases after ensureing；Dense uniform is formed in steel strip surface SiO2Film.High annealing interleaving agent of the coating using MgO as main component after decarburizing annealing.
Why the present invention uses the high annealing of secondary insulation, and annealing temperature is at 800~1120 DEG C, and preferably first Secondary annealing temperature when insulation 5~22 is small, and is pure nitrogen gas or nitrogen and hydrogen mixed gas in annealing atmosphere at 845~1095 DEG C Atmosphere under carry out, wherein, annealing temperature from when being warming up to 1050 DEG C for 850 DEG C control programming rate at 5~60 DEG C/h, Preferably programming rate is at 12~55 DEG C/h；When second of annealing temperature is at 1150~1230 DEG C, preferably move back for the second time Fiery temperature when insulation 5~30 is small at this temperature, and is carried out at 1150~1210 DEG C under perhydro atmosphere.In core of the present invention The high annealing one of held, using the high-temperature annealing process kept the temperature twice, the purpose is to：850~1050 DEG C are warming up to by two Secondary recrystallization forms single [110] (001) texture, in temperature-rise period, when annealing temperature is at 800~1120 DEG C, insulation 5~ 20 it is small when, strengthen suppressing the ability that first crystal grain is grown up, promote the perfect of secondary recrystallization；1000~1100 DEG C of formation Mg2SiO4 (magnesium silicate or forsterite) glass film bottom；1150~1230 DEG C of insulations carry out purification annealing, remove sulphur and nitrogen in steel, at the same time Subgrain annexes scattered remaining crystal grain, and subgrain tissue is more perfect, and crystal boundary is more straight.
Compared with prior art, the present invention under conditions of without nitriding process, by independent or compound addition Bi, P, One or more in Cu, Sn, Sb, Cr and As, and by 1000 DEG C of 1150 DEG C~1200 DEG C Low Temperature Hot Rollings and hot rolled plate~ 1150 DEG C of normalizing treatments, through once cold rolling and reduction ratio >=90%, decarburizing annealing, apply magnesia barrier coat, secondary insulation height After temperature annealing, stretching and leveling annealing and coating insulating coating, obtain finished steel plate magnetic induction density B 800 and be not less than 1.930T, iron P17/50≤1.08W/k is damaged, the high magnetic strength effect not less than 5% can drop relative to the prior art in cost, and magnetic property is stablized.
Embodiment
The present invention is described in detail below：
Table 1 is various embodiments of the present invention and the comparative example of comparative example；
Table 2 is various embodiments of the present invention and the main technologic parameters list of comparative example；
Table 3 is various embodiments of the present invention and comparative example performance text list.
Various embodiments of the present invention are produced according to following steps：
1）Routine smelts, is casting continuously to form base；
2）To heating strand, heating and temperature control is at 1150 ~ 1200 DEG C；
3）Segmentation carries out hot rolling, and it is 2.0~2.5mm to be rolled to thickness, and controls finishing temperature at 850 DEG C~1000 DEG C；
4）Batched, coiling temperature is no more than 600 DEG C；
5）Normalizing is carried out, normalizing temperature keeps the temperature 30~180s at this temperature at 1000 DEG C~1150 DEG C；
6）Disposable cold rolling is carried out after conventional pickling, and controlled rolling reduction ratio is not less than 90%；
7）Carry out decarburizing annealing, decarburization annealing temperature at 750~900 DEG C, soaking time in 60~180s, dew point at 23 ~ 27 DEG C, Protective atmosphere is H2And N2Wet mixed gas, wherein H2Volume content is 15~80%；
8）It is coated with the high annealing interleaving agent using MgO as main component；
9）Carry out the high annealing with secondary insulation：When annealing temperature rises to 800~1120 DEG C, first time insulation is carried out, Soaking time is in 5~22 hours；In this annealing stage, annealing atmosphere is pure nitrogen gas or the mixed gas of nitrogen and hydrogen, is mixed Close the percent by volume that hydrogen accounts in gas and be no more than 50%；Therebetween, from when being warming up to 1100 DEG C for 850 DEG C, control rises annealing temperature Warm speed is at 5~60 DEG C/h；
When annealing temperature rises to 1150~1230 DEG C, carry out second and keep the temperature, soaking time is in 5~30 hours, and complete Carried out under nitrogen atmosphere；
10）Carry out stretching and leveling and coating insulating coating.
The comparative example of 1 various embodiments of the present invention of table and comparative example（wt%）
As it can be seen from table 1 Als ＜ 0.010% in comparative example Q1, Als contents are relatively low, and AlN separates out quantity and reduces after decarburization, high Restraint reduces in temperature annealing；The solubility product of Als ＞ 0.015% in comparative example Q2, Als and N are higher, 1150 DEG C~1200 It is difficult to be dissolved completely under DEG C heating state, causes effectively to separate out quantity after decarburization and reduce, so as to cause restraint in high annealing Reduce；In comparative example Q8（P+ Cu+ Sn + Sb+ Cr+ As）＞ 0.80%, interface enriched element too high levels, hot-rolling edge cracking Greatly, production is difficult to smoothly carry out.
The main technologic parameters list of 2 various embodiments of the present invention of table and comparative example
1150 DEG C of hot rolling heating-up temperature ＜ in comparative example Q1,850 DEG C of finishing temperature ＜, AlN cannot be dissolved completely in heating process, And finishing temperature is relatively low, the AlN of bulky grain will be separated out, effective AlN, which is separated out, to be reduced, and normalizing time ＜ 30s, little particle AlN is not It can completely be dissolved, quantity is effectively separated out after decarburizing annealing and is reduced, so as to cause restraint in high annealing to reduce；In comparative example Q2 1200 DEG C of hot rolling heating-up temperature ＞, heating-up temperature is higher, casting blank crystal grains Size growth, so as to cause hot rolled plate, primary recrystallization Annealed sheet crystallite dimension is grown up, meanwhile, heating-up temperature is higher, will aggravate strand scaling loss, and lumber recovery reduces, normalizing time ＞ 180s, the normalizing time is too long will to cause favorably to separate out aggregation, roughening, thus cause rear process anneal in restraint reduce, meanwhile, Heating time is too long, and hot rolled plate crystal grain is grown up, so as to cause primary recrystallization annealed sheet crystallite dimension to be grown up；In comparative example Q8 often Change 1000 DEG C of temperature ＜, the AlN of normalizing small particles is difficult to be dissolved, and quantity is effectively separated out after decarburizing annealing and is reduced, so as to cause Restraint reduces in high annealing.
3 various embodiments of the present invention of table and comparative example performance text list
From table 3 it can be seen that conventional high temperature annealing process is used in comparative example Q1（Heat preservation method, 1150~1230 DEG C it Between keep the temperature, do not kept the temperature between 800~1120 DEG C）, secondary recrystallization temperature range heating time deficiency, secondary recrystallization cannot be complete Kind development, causes the reduction of final products magnetic property；Conventional high temperature annealing process is used in comparative example Q2（Heat preservation method, Keep the temperature between 1150~1230 DEG C, do not kept the temperature between 800~1120 DEG C）, secondary recrystallization temperature range heating time deficiency, two Secondary recrystallization, which cannot be improved, to be developed, and causes the reduction of final products magnetic property；Equally conventional high temperature lehr attendant is used in comparative example Q8 Skill（Heat preservation method, keeps the temperature between 1150~1230 DEG C, is not kept the temperature between 800~1120 DEG C）, secondary recrystallization temperature model Heating time deficiency is enclosed, secondary recrystallization, which cannot improve, to be developed, and causes the reduction of final products magnetic property.
Above-described embodiment is only the best example, and is not the restriction to embodiments of the present invention.

Claims (7)

1. a kind of economical high magnetic induction grain-oriented silicon steel, its component and weight percent content are：C：0.015~0.095%, Si： 2.80~3.60%, Als：0.010~0.015%, N：0.0050~0.0100%, Mn：0.010~1.00%, S：0.0030~ 0.0150%, Bi：0.0015~0.100%, one or both of addition P, Cu, Sn, Sb, Cr and As the compound of the above add Add, and meet that the sum of P, Cu, Sn, Sb, Cr and As are no more than 0.80%, remaining is iron and inevitable impurity.
A kind of 2. economical high magnetic induction grain-oriented silicon steel as claimed in claim 1, it is characterised in that：Component and weight as described below Degree is： N：0.005%~0.0095%, Mn：0.018%~0.93%, S：0.0030%~0.010%, Bi： 0.002%~0.09%.
3. a kind of production method of economical high magnetic induction grain-oriented silicon steel as claimed in claim 1, its step：
1）Routine smelts, is casting continuously to form base；
2）To heating strand, heating and temperature control is at 1150 ~ 1200 DEG C；
3）Segmentation carries out hot rolling, and it is 2.0~2.5mm to be rolled to thickness, and controls finishing temperature at 850 DEG C~1000 DEG C；
4）Batched, coiling temperature is no more than 600 DEG C；
5）Normalizing is carried out, normalizing temperature keeps the temperature 30~180s at this temperature at 1000 DEG C~1150 DEG C；
6）Disposable cold rolling is carried out after conventional pickling, and controlled rolling reduction ratio is not less than 90%；
7）Carry out decarburizing annealing, decarburization annealing temperature at 750~900 DEG C, soaking time in 60~180s, dew point at 23 ~ 27 DEG C, Protective atmosphere is H2And N2Wet mixed gas, wherein H2Volume content is 15~80%；
8）It is coated with the high annealing interleaving agent using MgO as main component；
9）Carry out the high annealing with secondary insulation：When annealing temperature rises to 800~1120 DEG C, first time insulation is carried out, Soaking time is in 5~22 hours；In this annealing stage, annealing atmosphere is pure nitrogen gas or the mixed gas of nitrogen and hydrogen, is mixed Close the percent by volume that hydrogen accounts in gas and be no more than 50%；Therebetween, from when being warming up to 1100 DEG C for 850 DEG C, control rises annealing temperature Warm speed is at 5~60 DEG C/h；
When annealing temperature rises to 1150~1230 DEG C, carry out second and keep the temperature, soaking time is in 5~30 hours, and complete Carried out under nitrogen atmosphere；
10）Carry out stretching and leveling and coating insulating coating.
4. a kind of method of economical high magnetic induction grain-oriented silicon steel is produced as claimed in claim 3, it is characterised in that：Heating strand Temperature is at 1100 ~ 1185 DEG C.
5. a kind of method of economical high magnetic induction grain-oriented silicon steel is produced as claimed in claim 3, it is characterised in that：Step 9）In When anneal for the first time, during annealing temperature is warming up to from 850 DEG C 1050 DEG C, control programming rate 12~55 DEG C/it is small When.
6. a kind of method of economical high magnetic induction grain-oriented silicon steel is produced as claimed in claim 3, it is characterised in that：Step 9）In First time annealing temperature is at 845~1095 DEG C.
7. a kind of method of economical high magnetic induction grain-oriented silicon steel is produced as claimed in claim 3, it is characterised in that：Step 9）In Second of annealing temperature is at 1150~1210 DEG C.
CN201711354380.9A 2017-12-15 2017-12-15 A kind of economical high magnetic induction grain-oriented silicon steel and production method Pending CN108018489A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201711354380.9A CN108018489A (en) 2017-12-15 2017-12-15 A kind of economical high magnetic induction grain-oriented silicon steel and production method

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201711354380.9A CN108018489A (en) 2017-12-15 2017-12-15 A kind of economical high magnetic induction grain-oriented silicon steel and production method

Publications (1)

Publication Number Publication Date
CN108018489A true CN108018489A (en) 2018-05-11

Family

ID=62074106

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201711354380.9A Pending CN108018489A (en) 2017-12-15 2017-12-15 A kind of economical high magnetic induction grain-oriented silicon steel and production method

Country Status (1)

Country Link
CN (1) CN108018489A (en)

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109554525A (en) * 2018-12-03 2019-04-02 武汉钢铁有限公司 A kind of manufacturing method of mirror surface-oriented silicon steel
CN110358896A (en) * 2019-05-23 2019-10-22 江苏北辰互邦电力股份有限公司 A kind of high magnetic strength transformer orientation silicon steel production decarburization annealing process
CN110791635A (en) * 2019-09-30 2020-02-14 鞍钢股份有限公司 Method for preparing high-magnetic-induction oriented silicon steel
CN110846576A (en) * 2019-11-18 2020-02-28 武汉钢铁有限公司 Oriented silicon steel with self-bonding performance and preparation method thereof
CN111334653A (en) * 2020-03-26 2020-06-26 武汉钢铁有限公司 High magnetic induction oriented silicon steel and preparation method thereof
CN113174468A (en) * 2021-04-30 2021-07-27 福建省奥克兰光电科技有限公司 Two-stage annealing process for high-temperature annealing and low-heat-preservation stage of oriented silicon steel bell-type furnace
CN115433869A (en) * 2022-09-23 2022-12-06 无锡普天铁心股份有限公司 Method for improving wide-direction magnetic uniformity of low-temperature high-magnetic-induction oriented silicon steel plate
CN115449741A (en) * 2022-09-20 2022-12-09 武汉钢铁有限公司 High-magnetic-induction oriented silicon steel produced based on continuous casting and rolling of thin slab and method
CN116804255A (en) * 2023-06-20 2023-09-26 武汉钢铁有限公司 Preparation method of high-magnetic-induction oriented silicon steel ultrathin strip with excellent adhesion

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695791A (en) * 2013-12-11 2014-04-02 武汉钢铁(集团)公司 High-magnetic strength oriented silicon steel and production method thereof
CN105274427A (en) * 2015-11-24 2016-01-27 武汉钢铁(集团)公司 High-magnetic-induction oriented silicon steel and production method

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695791A (en) * 2013-12-11 2014-04-02 武汉钢铁(集团)公司 High-magnetic strength oriented silicon steel and production method thereof
CN105274427A (en) * 2015-11-24 2016-01-27 武汉钢铁(集团)公司 High-magnetic-induction oriented silicon steel and production method

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109554525A (en) * 2018-12-03 2019-04-02 武汉钢铁有限公司 A kind of manufacturing method of mirror surface-oriented silicon steel
CN110358896A (en) * 2019-05-23 2019-10-22 江苏北辰互邦电力股份有限公司 A kind of high magnetic strength transformer orientation silicon steel production decarburization annealing process
CN110791635A (en) * 2019-09-30 2020-02-14 鞍钢股份有限公司 Method for preparing high-magnetic-induction oriented silicon steel
CN110846576A (en) * 2019-11-18 2020-02-28 武汉钢铁有限公司 Oriented silicon steel with self-bonding performance and preparation method thereof
CN110846576B (en) * 2019-11-18 2021-06-15 武汉钢铁有限公司 Oriented silicon steel with self-bonding performance and preparation method thereof
CN111334653B (en) * 2020-03-26 2022-03-15 武汉钢铁有限公司 High magnetic induction oriented silicon steel and preparation method thereof
CN111334653A (en) * 2020-03-26 2020-06-26 武汉钢铁有限公司 High magnetic induction oriented silicon steel and preparation method thereof
CN113174468A (en) * 2021-04-30 2021-07-27 福建省奥克兰光电科技有限公司 Two-stage annealing process for high-temperature annealing and low-heat-preservation stage of oriented silicon steel bell-type furnace
CN115449741A (en) * 2022-09-20 2022-12-09 武汉钢铁有限公司 High-magnetic-induction oriented silicon steel produced based on continuous casting and rolling of thin slab and method
CN115449741B (en) * 2022-09-20 2023-11-24 武汉钢铁有限公司 High-magnetic induction oriented silicon steel produced based on sheet billet continuous casting and rolling and method
CN115433869A (en) * 2022-09-23 2022-12-06 无锡普天铁心股份有限公司 Method for improving wide-direction magnetic uniformity of low-temperature high-magnetic-induction oriented silicon steel plate
CN115433869B (en) * 2022-09-23 2023-05-05 无锡普天铁心股份有限公司 Method for improving magnetic uniformity of low-temperature high-magnetic induction oriented silicon steel plate in width direction
CN116804255A (en) * 2023-06-20 2023-09-26 武汉钢铁有限公司 Preparation method of high-magnetic-induction oriented silicon steel ultrathin strip with excellent adhesion

Similar Documents

Publication Publication Date Title
CN107746942B (en) A kind of B800 &gt;=1.962T low temperature superelevation magnetic induction grain-oriented silicon steel and production method
CN108018489A (en) A kind of economical high magnetic induction grain-oriented silicon steel and production method
RU2378394C1 (en) Manufacturing method of sheet of texturated electrical steel with high magnetic induction
CN109112283A (en) The preparation method of low temperature high magnetic induction grain-oriented silicon steel
JP5351870B2 (en) Continuous casting method of non-oriented electrical steel strip
JP5939797B2 (en) Method for producing grain-oriented silicon steel by single cold rolling method
CN103805918B (en) A kind of high magnetic induction grain-oriented silicon steel and production method thereof
CN104561795A (en) High magnetic induction grain-oriented silicon steel with B800 being more than or equal to 1.94T and production method thereof
CN104451378B (en) A kind of orientation silicon steel having excellent magnetic characteristics and production method
MX2013005804A (en) Method for producing directional electromagnetic steel sheet.
CN105274427A (en) High-magnetic-induction oriented silicon steel and production method
JP6856179B1 (en) Manufacturing method of grain-oriented electrical steel sheet
CN103305748A (en) Non-oriented electrical steel plate and manufacturing method thereof
JP6663999B2 (en) Grain-oriented electrical steel sheet and its manufacturing method
CN105256226A (en) Cold-rolled non-oriented silicon steel low in iron loss and production method
CN107779727A (en) A kind of production method of orientation silicon steel
WO2017111547A1 (en) Grain oriented electrical steel sheet and method for manufacturing same
CN104726662B (en) Oriented electrical steel and its manufacture method
WO2019131853A1 (en) Low-iron-loss grain-oriented electrical steel sheet and production method for same
CN114082782A (en) Anti-wrinkling cold rolling method for 443 ultra-pure ferrite stainless steel
JP6079580B2 (en) Method for producing grain-oriented electrical steel sheet
CN111719078B (en) Production method of non-oriented silicon steel for eliminating corrugated defects
JP6947147B2 (en) Manufacturing method of grain-oriented electrical steel sheet
JP5920387B2 (en) Method for producing grain-oriented electrical steel sheet
JP5907202B2 (en) Method for producing grain-oriented electrical steel sheet

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
RJ01 Rejection of invention patent application after publication
RJ01 Rejection of invention patent application after publication

Application publication date: 20180511