CN107460292A - A kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance - Google Patents
A kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance Download PDFInfo
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- CN107460292A CN107460292A CN201710661356.3A CN201710661356A CN107460292A CN 107460292 A CN107460292 A CN 107460292A CN 201710661356 A CN201710661356 A CN 201710661356A CN 107460292 A CN107460292 A CN 107460292A
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- nitriding
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- 229910000976 Electrical steel Inorganic materials 0.000 title claims abstract description 46
- 230000006698 induction Effects 0.000 title claims abstract description 36
- 238000003672 processing method Methods 0.000 title claims abstract description 20
- 238000005121 nitriding Methods 0.000 claims abstract description 49
- 238000000137 annealing Methods 0.000 claims abstract description 41
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 39
- 239000010959 steel Substances 0.000 claims abstract description 39
- 239000013078 crystal Substances 0.000 claims abstract description 27
- 238000009749 continuous casting Methods 0.000 claims abstract description 23
- 238000009628 steelmaking Methods 0.000 claims abstract description 15
- 239000011248 coating agent Substances 0.000 claims abstract description 13
- 238000000576 coating method Methods 0.000 claims abstract description 13
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 10
- 238000005097 cold rolling Methods 0.000 claims abstract description 10
- 238000005266 casting Methods 0.000 claims abstract description 7
- -1 high annealing Substances 0.000 claims abstract description 5
- 239000008246 gaseous mixture Substances 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 11
- 238000003723 Smelting Methods 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 3
- 238000002791 soaking Methods 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 13
- 238000005516 engineering process Methods 0.000 abstract description 8
- 230000001629 suppression Effects 0.000 abstract description 8
- 238000004519 manufacturing process Methods 0.000 abstract description 7
- 239000002552 dosage form Substances 0.000 abstract description 5
- 239000003112 inhibitor Substances 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 6
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 230000002159 abnormal effect Effects 0.000 description 3
- 238000013019 agitation Methods 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 238000010924 continuous production Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 230000005856 abnormality Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 239000000395 magnesium oxide Substances 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
Classifications
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- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/125—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with application of tension
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
-
- 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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
-
- 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
- C22C38/18—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
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
- C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
- C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
- C23C8/24—Nitriding
- C23C8/26—Nitriding of ferrous surfaces
Abstract
The invention discloses a kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, belong to orientation silicon steel manufacturing technology field.Methods described includes steel-making, continuous casting, hot rolling, normalizing, cold rolling, decarburizing annealing, nitriding, coating annealing separating agent, high annealing, coating and stretching and leveling annealing, wherein：The strand equiaxial crystal ratio η of the casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；The temperature of the nitriding is 790 DEG C~980 DEG C, and total N content [N] is N in strip after nitridingl~330ppm.This method ensures a suppression of dosage form into depth and uniformity, effectively controls steel edge portion magnetic property exception caused by because line is brilliant and crystal grain is uneven, the finished strip quality of edges of acquisition is good, and magnetic property is excellent.
Description
Technical field
It is more particularly to a kind of to improve low temperature high magnetic induction grain-oriented silicon steel edge the present invention relates to orientation silicon steel manufacturing technology field
The processing method of performance.
Background technology
High magnetic induction grain-oriented silicon steel is important electrician's soft magnetic materials, is mainly used in large-scale power transformer and energy-efficient change
Manufacture unshakable in one's determination.Orientation strip property is uniformly transformer performance stabilization, most basic guaranteed conditions safe for operation.Traditional height
Magnetic induction grain-oriented silicon steel has two kinds of high-temperature technology and low temperature process.Low temperature high magnetic induction grain-oriented silicon steel technique is current high magentic induction oriented silicon
One of main technique of steel production, it has the advantages that energy consumption is low, lumber recovery is high, had excellent magnetic characteristics.Its main technique is：Steel-making
→ continuous casting → hot rolling → normalizing → cold rolling → decarburizing annealing → nitriding → high annealing → coating → stretching and leveling annealing etc., feature
It is that inhibitor is formed using acquired mode, i.e., by taking Nitrizing Treatment after decarburizing annealing, N element is penetrated into steel plate
In, and combine to form AlN inhibitor with the Als (dissolved aluminum) in steel.
Low temperature high magnetic induction grain-oriented silicon steel production technology window is extremely narrow, realizes that performance equal control difficulty is very big, especially exists
The high annealing stage because coil of strip is heated, unbalance stress easily causes steel edge portion property abnormality, is mainly shown as edge magnetic property
Difference, performance are unstable, or even influence Edge shape quality.Finished product macrostructure is characterized in that edge forms local fine grain band or two
Secondary recrystallization development imperfection or crystal particle dimension difference are larger.For this phenomenon, existing countermeasure generally by
Adjust high-temperature annealing process, adjustment high-temperature annealing furnace fired state, improve backplane type, to reduce coil of strip as far as possible in high annealing
During hot and cold temperature difference, so as to improve coil of strip magnetic property uniformity and quality of edges.But the technology realize difficulty compared with
Greatly, it is high to adjust risk, and above mentioned problem can not be fully solved.
The content of the invention
The present invention solves strip by providing a kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance
Edge line is brilliant, crystallite dimension inequality causes the abnormal technical problem of edge magnetic property.
In order to solve the above technical problems, improve adding for low temperature high magnetic induction grain-oriented silicon steel edge performance the invention provides a kind of
Work method, including continuous casting, hot rolling, normalizing, cold rolling, decarburizing annealing, nitriding, coating annealing separating agent, high annealing, coating and drawing
Whole annealing is stretched flat, wherein：
The strand equiaxial crystal ratio η of the casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；
The temperature of the nitriding is 790 DEG C~980 DEG C, and total N content [N] is N in strip after nitridingl~330ppm, wherein：
Nl=[Als]Steel-making-0.929[N]Steel-making+20；
In formula, NlFor the minimum nitriding amount of strip after nitriding, ppm；[Als]Steel-makingFor the quality with Als in steel smelting composition point
Number, ppm；[N]Steel-makingFor the mass fraction with N in steel smelting composition, ppm.
Further, the atmosphere of the nitriding is NH3、N2And H2Gaseous mixture.
Further, NH in the gaseous mixture3Volume accounting is 0.2%~20%, H2、H2And N2The volume ratio of gaseous mixture
VH2：VH2+N2=50%~75%.
Further, the equiaxial crystal ratio η calculates according to equation below：
Wherein：h0For the width of slab thickness direction equiax crystal, mm；
H is slab thickness, mm.
Further, the heating-up temperature of strand is 1000~1250 DEG C during the hot rolling.
Further, the reduction ratio of the cold rolling is not less than 80%.
Further, the temperature of the decarburizing annealing is 820 DEG C~850 DEG C, and the time is 50~150s.
Further, the temperature of the high annealing is 1100~1300 DEG C, and soaking time is 20~30h.
Further, the low temperature high magnetic induction grain-oriented silicon steel includes following components according to mass percent：C：0.05%~
0.09%；Si：2.9%~4.6%；Mn：0.05%~0.20%；S：0.005%~0.020%；Als：0.0225%~
0.0325%；N：0.0045%~0.0145%；Sn：0.01%~0.30%；Cr：0.01%~0.5%；Cu：0.01%~
0.8%；Remaining is Fe and inevitable impurity element.
One or more of embodiment of the present invention technical scheme, has at least the following technical effects or advantages：
The processing method provided in an embodiment of the present invention for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, including：Control
The strand equiaxial crystal ratio η of casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；The temperature for controlling nitriding is
790 DEG C~980 DEG C, total N content [N] is N in strip after nitridingl~330ppm.So that orientation silicon steel inhibitor is accurate, equal control
For target, by controlling the continuous casting steel degree of superheat and strand equiaxial crystal ratio, improve structural homogenity and the distribution of effective precipitate is equal
Even property, ensures a suppression of agent and is formed uniformly；By controlling nitriding temperature and nitriding content, ensure a suppression of dosage form into depth and uniformly
Property, effectively controlling steel edge portion magnetic property exception and plate shape caused by because line is brilliant and crystal grain is uneven deteriorates, acquisition into
Product steel edge portion plate shape is good, and magnetic property is excellent.
Brief description of the drawings
Fig. 1 is the schematic cross-section of low temperature high magnetic induction grain-oriented silicon steel strip strand of the embodiment of the present invention；
Fig. 2 is the low temperature high magnetic induction grain-oriented silicon steel edge macrostructure figure that the embodiment of the present invention obtains；
Fig. 3 is the low temperature high magnetic induction grain-oriented silicon steel edge fine grain macrostructure figure that comparative example of the present invention obtains.
In figure, 1- columnar zones；The isometric crystalline regions of 2-；3- solidifies Delta Region.
Embodiment
The embodiment of the present invention provides a kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, solves band
The technical problem that steel edge line is brilliant, crystallite dimension inequality causes edge magnetic property and plate shape is abnormal, the finished strip edge of acquisition
Quality is good.
In order to solve the above technical problems, general thought of the embodiment of the present invention is as follows：
The invention provides a kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, including continuous casting, heat
Roll, normalizing, cold rolling, decarburizing annealing, nitriding, coating annealing separating agent, high annealing, coating and stretching and leveling annealing, wherein：
The strand equiaxial crystal ratio η of the casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；
The temperature of the nitriding is 790 DEG C~980 DEG C, and total N content [N] is N in strip after nitridingl~330ppm, wherein：
Nl=[Als]Steel-making-0.929[N]Steel-making+20；
In formula, NlFor the minimum nitriding amount of strip after nitriding, ppm；[Als]Steel-makingFor the quality with Als in steel smelting composition point
Number, ppm；[N]Steel-makingFor the mass fraction with N in steel smelting composition, ppm.
The application can be seen that by controlling the continuous casting steel degree of superheat and strand equiaxial crystal ratio by above content, improve
Structural homogenity and effective precipitate distributing homogeneity, ensure a suppression of agent and are formed uniformly；By controlling nitriding temperature and nitriding to contain
Amount, ensures a suppression of dosage form into depth and uniformity.The application using orientation silicon steel inhibitor is accurate, equal control as target, pass through
To orientation silicon steel inhibitor uniformity controlling, it is abnormal effectively to control edge magnetic property caused by because line is brilliant and crystal grain is uneven
And plate shape deteriorates, the finished strip edge of acquisition is good without fine grain, plate shape.
In order to be better understood from above-mentioned technical proposal, below by accompanying drawing and specific embodiment to technical solution of the present invention
It is described in detail, it should be understood that the specific features in the embodiment of the present invention and embodiment are to the detailed of technical solution of the present invention
Thin explanation, rather than the restriction to technical solution of the present invention, in the case where not conflicting, the embodiment of the present invention and embodiment
In technical characteristic can be combined with each other.
The embodiment of the present invention provide it is a kind of improve low temperature high magnetic induction grain-oriented silicon steel edge performance processing method, suitable for
AlN is the low temperature high magnetic induction grain-oriented silicon steel of major inhibitors, and the low temperature high magnetic induction grain-oriented silicon steel includes according to mass percent
Following components：C：0.05%~0.09%；Si：2.9%~4.6%；Mn：0.05%~0.20%；S：0.005%~
0.020%；Als：0.0225%~0.0325%；N：0.0045%~0.0145%；Sn：0.01%~0.30%；Cr：
0.01%~0.5%；Cu：0.01%~0.8%；Remaining is Fe and inevitable impurity element.Its processing method includes refining
Steel, continuous casting, hot rolling, normalizing, cold rolling, decarburizing annealing, nitriding, coating annealing separating agent, high annealing, coating and stretching and leveling are moved back
Fire, wherein：
The strand equiaxial crystal ratio η for controlling the casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；
The temperature for controlling the nitriding is 790 DEG C~980 DEG C, and total N content [N] is N in strip after nitridingl~330ppm,
Wherein：Nl=[Als]Steel-making-0.929[N]Steel-making+20；
In formula, NlFor the minimum nitriding amount of strip after nitriding, ppm；[Als]Steel-makingFor the quality with Als in steel smelting composition point
Number, ppm；[N]Steel-makingFor the mass fraction with N in steel smelting composition, ppm.
In the present embodiment, the atmosphere of the nitriding is NH3、N2And H2Gaseous mixture.Wherein, NH3Account for the volume of total gaseous mixture
Than for 0.2%~20%, the volume ratio V of hydrogen, hydrogen and nitrogen mixtureH2：VH2+N2=50%~75%.NH3At high temperature,
Cracked by catalyst of Fe, generate active N atoms, active N atoms are absorbed by silicon steel sheet so as to realize nitriding.Oozed by regulation
Nitrogen temperature, nitriding time and NH3Content can realize to after nitriding in strip N content control, ensure nitriding after strip width side
To N content deviation ＜ 25ppm, be advantageous to the uniformity that inhibitor is formed.
In the present embodiment, the equiaxial crystal ratio η calculates according to equation below：
As shown in figure 1, wherein：h0For the width of slab thickness direction equiax crystal, mm；H is slab thickness, mm.Coagulated in figure
Gu Delta Region 3 is the application region to be controlled, for example, can be in continuous casting two cold region by way of taking electromagnetic agitation
Equiaxial crystal ratio is controlled in the range of 10%~40%.Certainly, simply the control mode of equiaxial crystal ratio is illustrated herein,
This control mode is not limited to, enterprise can make equiaxial crystal ratio maintain 10%~40% according to own characteristic using any
Mode.
In the present embodiment, the heating-up temperature of strand is 1000~1250 DEG C during the hot rolling.
In the present embodiment, the reduction ratio of the cold rolling is not less than 80%.
In the present embodiment, the decarburization annealing temperature is 820 DEG C~850 DEG C, and the time is 50~150s, steel plate carbon after decarburization
Content is no more than 30ppm.
In the present embodiment, the temperature of the high annealing is 1100~1300 DEG C, and soaking time is 20~30h.
The principle of the application is elaborated below.
The core of orientation silicon steel Properties Control is inhibitor control, and can process inhibitor, which accurately control, directly determines and take
It is good and bad to the performance of silicon steel.Low temperature high magnetic induction grain-oriented silicon steel requires more harsh to being precisely controlled for inhibitor.On the one hand, make steel
The accurate control of the compositions such as technique Als, N be the basis of inhibitor, strand composition and structural homogenity to inhibitor uniformity and
Primary recrystallization control has significant impact；On the other hand, depth, state of the strip in nitriding stage N element infiltration steel plate
And the uniformity is an important factor for influenceing the effect of high annealing inhibitor.
The application why controls the continuous casting steel degree of superheat for 10~30 DEG C and control strand equiaxial crystal ratio 10%~
40%, being on the one hand to, which reduces strand leptoprosopy, nearby solidifies the element segregation of Delta Region 3, improves Elemental redistribution uniformity；Separately
On the one hand, control that a certain proportion of equiaxial crystal ratio can improve the zone freezing structural homogenity and effective precipitate is evenly distributed
Property.Above-mentioned requirements are the bases that rear process inhibitor is formed uniformly.
Why the application controls higher 790~980 DEG C of nitriding temperature, is because being experimentally confirmed, in the humidity province
Between nitriding enough depth and more uniform crystalline state (Al, Si) N inhibitor can be formed in steel plate thickness direction within a short period of time；
Strip nitrogen content is N after why requiring Nitrizing Treatmentl~330ppm, is passed through NH3Volume ratio is 0.2%~20%, is to suppress
Dosage form ensures a suppression of agent and is evenly distributed in plate width direction into the sufficient N element of offer, so as to be finished strip width magnetic
The uniformity of performance lays the foundation, and N content easily causes surface defect more than 330ppm.
By the above as can be seen that the application mainly using orientation silicon steel inhibitor is accurate, equal control as target, lead to
The control to continuous casting and nitriding procedure technology is crossed, oriented silicon steel band steel plate cross direction performance uniformity is improved, avoids distance
Because steel edge portion magnetic property caused by the defects of line is brilliant, crystallite dimension inequality is different in the range of 0~100mm of finished strip edge
Often, plate shape deterioration problem.
In order that those skilled in the art can further understand the scheme of the embodiment of the present invention, will be based on below
The scheme that the embodiment of the present invention is introduced describes in detail to it.
The production method of the low temperature high magnetic induction grain-oriented silicon steel strip of the present embodiment, specifically includes following steps：
S1：Steel-making, continuous casting strand, 10~30 DEG C of the continuous casting steel degree of superheat, electromagnetic agitation control are used in two cold-zone domains
Equiaxial crystal ratio η=10%~40% processed, 30~400A of electric current of electromagnetic agitation, 1~10Hz of frequency；
S2：Strand is heated, heating-up temperature is 1000~1250 DEG C, carries out hot rolling afterwards, hot rolling include roughing and
Finish rolling, finish rolling entrance enable strip edge heater, and hot rolling plate thickness is 1.5~3.5mm；
S3：Using two-part normalizing, the full blanket of nitrogen of dry type, pickling removal scale on surface after normalizing；
S4：Cold rolling, reduction ratio are not less than 80%；
S5：Decarburizing annealing, decarburization annealing temperature are 820 DEG C~850 DEG C, and the decarburizing annealing time is 50~150s；
S6：Nitrizing Treatment, nitriding temperature are 790~980 DEG C, atmosphere NH3、N2、H2Gaseous mixture, NH in gaseous mixture3Body
Product accounting is 0.2%~20%, H2、H2And N2The volume ratio V of gaseous mixtureH2：VH2+N2=50%~75%, it is total in strip after nitriding
N content [N] is Nl~330ppm, and strip width direction N content deviation ＜ 25ppm；
S7：Apply coated with the annealing separating agent based on magnesia；
S8：High annealing is carried out, high temperature section annealing temperature is 1100~1300 DEG C, is incubated 20~30h；
S9：Stretching and leveling annealing is carried out after coating insulating coating.
Each embodiment and comparative example continuous casting and process parameter for nitriding are as shown in table 1.
The embodiment of table 1 and comparative example continuous casting and process parameter for nitriding list
The performance test results of the low temperature high magnetic induction grain-oriented silicon steel of each embodiment and comparative example production are as shown in table 2.
The embodiment of table 2 and comparative example magnetic property, edge line crystalline substance and plate shape list
Note：The plate width direction iron loss deviation=wide middle part iron loss of plate width direction iron loss extreme difference/plate
The high magnetic induction grain-oriented silicon steel magnetic property produced it can be seen from table 2 and Fig. 2-3 using the present processes is excellent
Different, steel plate width direction magnetic property is uniform, and edge is good without fine grain, plate shape.And comparative example is using the technology outside the application scope
Parameter, finished steel plate width magnetic property lack of homogeneity, and there is edge line crystalline substance and edge flanging phenomenon.
One or more of embodiment of the present invention technical scheme, has at least the following technical effects or advantages：
The processing method provided in an embodiment of the present invention for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, including：Control
The strand equiaxial crystal ratio η of casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；The temperature for controlling nitriding is
790 DEG C~980 DEG C, total N content [N] is N in strip after nitridingl~330ppm.So that orientation silicon steel inhibitor is accurate, equal control
For target, by controlling the continuous casting steel degree of superheat and strand equiaxial crystal ratio, improve structural homogenity and the distribution of effective precipitate is equal
Even property, ensures a suppression of agent and is formed uniformly；By controlling nitriding temperature and nitriding content, ensure a suppression of dosage form into depth and uniformly
Property, effectively controlling steel edge portion magnetic property exception and plate shape caused by because line is brilliant and crystal grain is uneven deteriorates, acquisition into
Product steel edge portion plate shape is good, and magnetic property is excellent.
It should be noted last that above embodiment is merely illustrative of the technical solution of the present invention and unrestricted,
Although the present invention is described in detail with reference to example, it will be understood by those within the art that, can be to the present invention
Technical scheme modify or equivalent substitution, without departing from the spirit and scope of technical solution of the present invention, it all should cover
Among scope of the presently claimed invention.
Claims (9)
1. a kind of processing method for improving low temperature high magnetic induction grain-oriented silicon steel edge performance, including it is continuous casting, hot rolling, normalizing, cold rolling, de-
Carbon annealing, nitriding, coating annealing separating agent, high annealing, coating and stretching and leveling annealing, it is characterised in that：
The strand equiaxial crystal ratio η of the casting process is 10%~40%, and the continuous casting steel degree of superheat is 10~30 DEG C；
The temperature of the nitriding is 790 DEG C~980 DEG C, and total N content [N] is N in strip after nitridingl~330ppm, wherein：Nl=
[Als]Steel-making-0.929[N]Steel-making+20；
In formula, NlFor the minimum nitriding amount of strip after nitriding, ppm；[Als]Steel-makingFor the mass fraction with Als in steel smelting composition,
ppm；[N]Steel-makingFor the mass fraction with N in steel smelting composition, ppm.
2. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 1, it is characterised in that institute
The atmosphere for stating nitriding is NH3、N2And H2Gaseous mixture.
3. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 2, it is characterised in that institute
State NH in gaseous mixture3Volume accounting is 0.2%~20%, H2、H2And N2The volume ratio V of gaseous mixtureH2：VH2+N2=50%~75%.
4. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 3, it is characterised in that institute
Equiaxial crystal ratio η is stated to be calculated according to equation below：
<mrow>
<mi>&eta;</mi>
<mo>=</mo>
<mfrac>
<mrow>
<mi>h</mi>
<mn>0</mn>
</mrow>
<mi>h</mi>
</mfrac>
<mo>&times;</mo>
<mn>100</mn>
<mi>%</mi>
</mrow>
Wherein：h0For the width of slab thickness direction equiax crystal, mm；
H is slab thickness, mm.
5. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 3, it is characterised in that institute
The heating-up temperature of strand is 1000~1250 DEG C when stating hot rolling.
6. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 3, it is characterised in that institute
The reduction ratio for stating cold rolling is not less than 80%.
7. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 3, it is characterised in that institute
The temperature for stating decarburizing annealing is 820 DEG C~850 DEG C, and the time is 50~150s.
8. the processing method of low temperature high magnetic induction grain-oriented silicon steel edge performance is improved as claimed in claim 3, it is characterised in that institute
The temperature for stating high annealing is 1100~1300 DEG C, and soaking time is 20~30h.
9. the processing method of the raising low temperature high magnetic induction grain-oriented silicon steel edge performance as described in one of claim 1-8, its feature
It is, the low temperature high magnetic induction grain-oriented silicon steel includes following components according to mass percent：C：0.05%~0.09%；Si：
2.9%~4.6%；Mn：0.05%~0.20%；S：0.005%~0.020%；Als：0.0225%~0.0325%；N：
0.0045%~0.0145%；Sn：0.01%~0.30%；Cr：0.01%~0.5%；Cu：0.01%~0.8%；Remaining is
Fe and inevitable impurity element.
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