CN107974620A - A kind of yield strength >=600Mpa high speed rotor of motor non-orientation silicon steel and production method - Google Patents
A kind of yield strength >=600Mpa high speed rotor of motor non-orientation silicon steel and production method Download PDFInfo
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- CN107974620A CN107974620A CN201711245381.XA CN201711245381A CN107974620A CN 107974620 A CN107974620 A CN 107974620A CN 201711245381 A CN201711245381 A CN 201711245381A CN 107974620 A CN107974620 A CN 107974620A
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- 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
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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
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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
- C21D8/1244—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- 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
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- 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
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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Abstract
A kind of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels, its chemical composition are calculated as by wt%：C：0.001 0.003%, Si：2.6 3.4%, Mn：0.20 0.60%, P≤0.005%, S≤0.005%, Als：0.75 0.95%, N：0.002 0.006%, Nb：0.053‑0.20%.Production stage：Through converter smelting and it is cast into base；Continuous casting billet is heated；Conventional roughing and finish rolling；Normalizing；Cold rolling is carried out after pickling；Continuous annealing.End properties of the thickness of the present invention no more than 0.35mm are in yield strength >=600MPa, tensile strength >=700MPa, P1.0/400≤ 35W/kg, B5000≥1.60T。
Description
Technical field
The present invention relates to non-oriented electrical steel manufacturing technology, and in particular to a kind of high rotating speed rotor non-orientation silicon steel and its
Production method, it is suitable for high intensity non-orientation silicon steel production of the finished product thickness no more than 0.35mm.
Background technology
Permanent magnet synchronous motor is mainly made of the stator of winding and the rotor of configuration permanent magnet, with internal rotor embedment forever
Magnet is mainstream, is known as ipm motor, is the motor with intelligent power module.
At present, due to the rapid development of electronic technology, rotating speed in mechanical equipment with motor is towards can any controlling party
To development, to realize high speed.And as the electromagnetic steel plate of core material in motor, its desired frequency used be no longer with
Past 50Hz or the power frequency of 60Hz, but to be used under high frequency environment, i.e., it can be run under 400Hz to thousands of Hz.Therefore, from
From the point of view of product, current product cannot be met the requirements.New requirement also wants rotating speed to be not less than 10000 revs/min, this makes to turn
Son not only increases centrifugal force in the case where running at high speed, and because the stress that the change of rotating speed is born also is changing.Therefore to turning
The mechanical performance of the core material of son there has also been higher requirement.Particularly ipm motor, rotor it is complex-shaped, should consider
The stress concentration of rotor, is considered and the mechanical performance such as centrifugal force while stress of variation again.In addition, in robot and other
Servo motor used in Work machine field is similarly because requirement of the high speed to electromagnetic steel plate of rotating speed is also more and more high.
The excellent electromagnetic steel plate of this magnetic property and mechanical performance is how manufactured, there are many documents all to report, mainly
Several classes can be divided into by improving the method for non-orientation silicon steel mechanical strength：Precipitation strength, solution strengthening, dislocation strengthening and the above are strong
Change mechanism it is composite intensified.
Electrical sheet component used in motor is usually all Ultra-low carbon, nitrogen（Mass fraction is respectively less than 50ppm）With high silicon
（2.4%-3.5%）, also need to add high Al sometimes to ensure that its excellent magnetic property is particularly low iron loss.High rotating speed driving electricity
The confidential electrical sheet asked will more traditional high more than 200MPa of non-oriented electrical steel intensity, and improve intensity and also need to protect at the same time
Card cannot damage its excellent magnetic property.
In the prior art, magnetic property silicon steel is to improve intensity by the solution strengthening of Si, Al to reduce iron loss at the same time, it is deposited
It is harsh in production technology, cause cold rolling difficult due to Si contents higher；The Al of higher can greatly increase steel-making difficulty.Therefore
Common high strength construction steel using the strengthening mechanism such as solid solution and precipitation, can effectively improve intensity, but its magnetic property is poor more.Therefore need
Non-oriented electrical steel intensity is improved by a variety of strengthening mechanisms.
The Japanese high intensity non-oriented electrical steel that began one's study from 1980, represents producer and is mainly Nippon Steel, JFE and lives
Friendly metal.
In terms of solution strengthening improves non-oriented electrical steel intensity, Nippon Steel is main in disclosed patent before nineteen ninety
Using solution strengthening such as Si, P, Mn, Ni, other alloying elements such as Cr, Mo, Cu, Ti can be also used sometimes, and to reach high-strength
Degree generally can suitable control production board crystallite dimension.
In terms of precipitation strength improves non-oriented electrical steel intensity, since past solution strengthening is often containing expensive gold
Belong to nickel, cause cost of alloy significantly to rise, and solution strengthening adds the intensity before rolling so that rolling difficulty increase, because
United States Patent (USP) of this Sumitomo Metal Industries in 2011（US 7,922.834 B2,2011-04-12）In propose to non-orientation silicon steel
The middle method for adding this kind of microalloy element of Nb, Ti, V, Zr, is carried by forming tiny carbide particle by precipitation strength
High intensity.
Start to use other schedule of reinforcements after nineteen ninety, in patent disclosed in Nippon Steel.On the basis of solution strengthening
Zr, Ti are used at the same time, and V Carbonitride Precipitations are strengthened.In general, carbonitride severe exacerbation magnetic property in order to prevent, patent
In have strict requirements to the contents of these elements.In addition, addition Ni can increase the cost of steel, select to be not added with many patents
Ni。
The reinforcing effect of various carbonitrides is also not quite similar, and Kubo Tian Meng thinks the carbonitride of Zr and other carbonitrides
Compare, precipitating reinforcing effect is big, while the deterioration to magnetic property is smaller（2003-342698,2003-12-03）.
The research steering of the last decade Nippon Steel precipitation strength of Cu metal phases, such as Japan Patent 2008-
261053.2008-10-30 the and its document of the Publication No. CN102007226A in China's application.Cu metal phases reduce saturation
The effect very little of magnetic flux density, and compared with carbonitride, it is smaller to the inhibition of magnetic domain wall moving.Using Cu metal phases
Precipitation strength when, by controlled rolling and controlled cooling Cu metal phases before cold rolling can be made not separate out, or do not separate out too much, or control
Its precipitation state, so that hot rolled plate or normalizing plate are unlikely to harden and embrittlement especially bigly, is thus easier cold rolling,
Reduce the generation rolled and split during cold rolling.
From the analysis to document cited above, draw and Si, Ni content are for example improved using solution strengthening, although finished product
Magnetism will not deteriorate, but cost of alloy significantly rises, and largely addition solid solution element will increase the intensity before rolling, with
The reduction of cold rolling finished product thickness, processing hardening clearly will be easy to that broken belt occurs in cold rolling, brought to production very big
It is difficult.
Precipitation strength is carried out using Cu, when Cu contents are below 1%, the precipitation strength effect of Cu is extremely limited, and Cu contents increase
Adding causes the increase of age-hardening amount, and precipitate uneven dispersion when Cu contents are more than 3% during finished products separates out, at timeliness heat
Intensity declines after reason, and magnetic flux density reduces.The brittle failure of steel plate when Cu too high levels also result in Surface Defects in Steel Plate and cold rolling.
In addition, the complex intensifying of a variety of alloying elements, will increase the difficulty of steelmaking alloy, the addition of a variety of alloys will draw
Enter more complicated complex inclusion, the component and size of these complex inclusions are difficult to be effectively controlled, will seriously hinder
Properties of product.The addition of more alloys will also increase the time of steelmaking alloy, influence rhythm of production, and bring the temperature drop of higher.
In order to meet suitable cast temperature, it is necessary to improve Tapping Temperature of Bof, not only increase energy consumption, be also unfavorable for going for harmful element
Remove.And after a variety of complex intensifying element additions, in order to guarantee fully to be dissolved, complex intensifying element can be played
Effect is, it is necessary to which the hot rolling heating-up temperature of higher, this is unfavorable to magnetic property, while also increases hot rolling energy consumption.And the hot rolling of higher
If temperature is without control, after hot rolling reeling and in normalizing, precipitate will agglomeration, do not have disperse point
Cloth is so as to improve the effect of intensity.
Americana US20090202383, it discloses a kind of non-orientation silicon steel and its manufacture method.Pass through addition
Cu, Ni, Cr, Mo, elements such as w, progress matrix solution strengthening and Second Phase Precipitation are strengthened to improve yield strength, but this method magnetic
Poor-performing, cost are higher.
In addition, many Chinese patents also refer to much methods on improving non-orientation silicon steel intensity.
Chinese patent CN103173678A discloses a kind of rotor non-orientation silicon steel and its manufacture method.By traditional high
A small amount of boron is added in grade non-oriented silicon steel（B≤0.005%）, main alloy element satisfaction 4.1%≤（Si+Al/2+Mn）≤
6.0%, also by Calcium treatment take off S (S≤10ppm) and 850 ~ 900 DEG C × 90S normalizing,>100 DEG C of warm-rollings, 920 ~ 950 DEG C × 20S
The technological means such as recrystallization annealing, realize fine magnetic property (B5000 >=1.66T, P1.5/50≤2.70W/kg, anisotropy≤
And high intensity 9%)（Yield strength >=420MPa, Low Cycle Fatigue Strength >=420MPa）.Document main problem is yield strength
Low, difficulty of processing is big.
Chinese patent CN103409684A discloses a kind of high strength cold-rolled magnetic pole steel and preparation method thereof.By adding C：
0.05~0.07%、Mn：1.0~1.2%、Si：0.3~0.5%、Als：0.02 ~ 0.07%, the chemistry such as Ti≤0.04%, Nb≤0.04% member
Element, and by obtaining high intensity and high magnetic induction performance in continuous annealing+flattening process.But it is smooth after iron loss it is very high, and
Smooth process adds cost.
Chinese patent CN201010278193.9 provides a kind of high-magnetic induction non-oriented electrical steel containing vanadium and titanium, its chemistry into
It is C to divide percentage by weight：0.001-0.005%, Si：0.50-0.65%, Mn：0.15-0.35%, P≤0.025%, S≤
0.008%th, Als：＜ Ti≤0.01% of 0.25-0.35%, N≤0.007%, 0,0 ＜ V≤0.01%, surplus are Fe and can not
The impurity avoided, by rational composition design, reduces the precipitation of the vanadium titanium carbon nitride of small and dispersed.Its preparation method, adds
Hot temperature is 1130-1160 DEG C；Finish rolling start rolling temperature for >=1020 DEG C, finishing temperature be 870-910 DEG C, coiling temperature for >=
650℃.By suppressing the adverse effect of vanadium titanium, the non-oriented electrical steel containing vanadium and titanium for meeting electromagnetic performance requirement can be produced.But
The document in being the design of low grade non-oriented silicon steel, the index such as yield strength and magnetic property cannot meet pot motor rotor
It is required that.
Chinese patent (application number：201310420802.3) the fine magnetic property No yield point electricity of Rm >=600MPa a kind of is provided
Work steel and its production method.Its composition by weight percent content is：Si：2.5-3.5%, Mn：0.1-1.0%, Ni+Al are no more than
1.0%, N≤0.005%, S≤0.015%, C≤0.003%, P≤0.05%, remaining is iron and residual content；And to meet：1.0
≤Al/Ni≤2.0；Performance：Rm >=600MPa, Rel >=500MPa, P1.0/400≤ 17 W/kg, B5000≥1.66T.The document is
High-revolving driving design of electrical motor, it is desirable to which high frequency iron loss is low, and high intensity is obtained by the solution strengthening of the elements such as Ni and Al.The party
Although the performance that method finally obtains disclosure satisfy that the requirement of high intensity and low iron loss, but due to adding the valuable gold more than 0.3%
Belong to Ni, cost of alloy is very high.And excessive alloy amount will cause cold rolling difficulty increase, it is necessary to using the means such as warm-rolling into
Row production, is unfavorable for producing in enormous quantities.
Chinese Patent Application No. is 200910049782.7 document, there is provided a kind of system of 500Mpa grade cold rolled magnetic pole steels
Method is made, its composition by weight percent content is：C：0.07 ~ 0.1%, Si：0.18 ~ 0.31%, Mn：1.00 ~ 1.50%, P≤
0.02%, S≤0.007%, O≤0.004%, N≤0.004%, Nb：0.046 ~ 0.06%, Ti≤0.003%, V：0.050 ~ 0.070%,
Surplus is Fe and inevitable impurity；Performance：Rm >=570MPa, B5000 >=1.570T, but this steel grade is used as magnetic pole steel, and
Do not consider to control iron loss, from the component of patent, due to the component system using low silicon high-manganese, its iron loss will be very high,
It can not meet that high speed rotor still keeps the requirement of relatively low iron loss in high frequency, be only capable of using as magnetic pole steel.
The content of the invention
In view of the deficiencies of the prior art, the present invention provides a kind of end properties of thickness no more than 0.35mm in yield strength
>=600MPa, tensile strength >=700MPa, P1.0/400≤ 35W/kg, B5000The high speed rotor of motor non-orientation silicon steel of >=1.60T
And production method.
Realize the measure of above-mentioned purpose：
A kind of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels, its chemical composition are by weight percentage：C：
0.001-0.003%, Si：2.6-3.4%, Mn：0.20-0.60%, P≤0.005%, S≤0.005%, Als：0.75-0.95%, N：
0.002-0.006%, Nb：0.053-0.20%, remaining is iron and residual content；And to meet at the same time：4.5%≤Si+2Als-
0.5Mn+2.92P≤5.0%, solid solution niobium Nb*0.04% ＜ Nb of content*% ＜ 0.08%, Nb*%=(Nb/93-C/12-N/14) * 100,
1≤N/C≤3。
Preferably：The weight percent content of Nb is 0.063-0.185%.
Further preferably：The weight percent content of Nb is 0.08-0.176%.
Preferably：The weight percent content of N is 0.0043-0.0055%.
Preferably：It is dissolved niobium Nb*0.046% ＜ Nb of content*% ＜ 0.073%.
Preferably：The ratio of N and C is controlled in 1≤N/C≤2.
Produce a kind of method of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels, its step：
1）Through converter smelting and it is cast into base；
2）Continuous casting billet is heated, control soaking temperature is at 1100-1150 DEG C, time inside furnace 2-4h；
3）Carry out conventional roughing and finish rolling, and after controlling hot rolling plate thickness in 2.10 ± 0.05mm；
4）Normalizing is carried out, control normalizing soaking temperature is at 840-940 DEG C, and soaking time is in 20-60s；
5）Cold rolling is carried out after pickling：Mill product finished product thickness is no more than 0.35mm；
6）Continuous annealing is carried out, and controls soaking temperature for soaking time in 60-120s, atmosphere is pure dry N at 750-820 DEG C2。
Preferably：Normalizing soaking temperature is at 860-920 DEG C.
The effect of the main intensified element such as C, Mn, Si, Nb and mechanism in the present invention：
C:0.001-0.003%
In steel C as solid solution carbon or cementite have larger infringement to magnetic property, therefore it is required that C be no more than 0.0030%, meanwhile, be
Ensure there is a certain amount of a NbC and Nb（C, N）Compound, C are not less than 0.001%.
N：0.002-0.006%
N has magnetic property larger infringement in steel, therefore it is required that N≤0.0060%.And nitride and carbonitride be to crystal grain thinning,
Improving intensity has very important effect, and particularly nitride has significant effect, and therefore, it is necessary to certain N to be formed
Compound, it is desirable to N >=0.002%, preferably 0.0020%≤N≤0.0030%.It is because C members why to limit 1≤[N]/[C]≤3
If element is excessive, it will produces magnetic aging, magnetic property can deteriorate after long service.But also need to a small amount of C, can with N,
Nb forms NbN or Nb together（C, N）Compound, plays crystal grain thinning, improves the effect of intensity.Because nitride crystal grain thinning
Effect is more obvious, it requires that N content should be higher than that C content, preferably 1≤[N]/[C]≤2.But consider that N is easily formed more at the same time
Dissipate tiny AlN hinders crystal grain to grow up strongly, deteriorates iron loss, therefore present invention provide that N≤0.0060%.
Si：2.6-3.4%
Si can improve resistivity, reduce iron loss；Si is also solution strengthening element, can significantly improve yield strength, excessive Si meetings
Cause rolling difficult, present invention provide that Si：2.6-3.4%, to ensure certain yield strength and stable rolling performance, preferably
Si:3.0-3.2%。
Why the present invention limits+2.92 [%P]≤5.0 of 4.5≤[%Si]+2 [%Als] -0.5 [%Mn], is to ensure
Enough resistivity is to reduce eddy-current loss, it is necessary to assure certain alloy content, but alloy content is excessive is analysed plus Nb elements
Go out the effect of reinforcing, the hot rolling plate strength after normalizing is excessive, and cold rolling load is excessive easily to produce broken belt.
Mn：0.20-0.60%
Mn can significantly improve the yield strength and fatigue strength of steel plate, but Mn can not be excessive as displaced type solid solution element.Cause
Hot rolling fluctuation is easily caused for excessive Mn, is unfavorable for template precision controlling.Meanwhile some researches show that, NbC usually with
When the compound precipitations of MnS, Mn and proportional C content, be conducive to the tiny intensive precipitations of NbC, enhancing suppresses the work that crystal grain is grown up
With so as to obtain high intensity and toughness.
Al: 0.75-0.95%
Al dissolves in ferrite and improves resistivity reduction iron loss, while energy deoxidation fixed nitrogen, but be easy to cause oxygen in production board top layer
Change；Al can improve yield strength, but high Al can make smelting casting difficult.Therefore present invention provide that Als：0.75-0.95%.
P：≤0.01%
P is solution strengthening element, can also improve the resistivity of material, but P is excessive steel plate is become fragile, and increases the wind of cold rolling broken belt
Danger.
S: ≤0.005%
S is the harmful element in steel, significantly reduces fatigue strength, but adding Mn elements can improve MnS solid solubility temperatures, make MnS
Roughening, therefore can suitably relax the limitation of S, reduce steel-making cost.In addition, Mn is also roughened MnS, is conducive to crystal grain and grows up.Therefore
Present invention provide that S≤0.005%.
Nb:0.04-0.20%
Nb is a kind of carbide, is mainly existed in steel with carbonitride form, the disperse in ferrite matrix
It is dispersed with the tiny spherical precipitate Nb of substantial amounts of a diameter of tens nanometers（C, N）, solute atoms is produced in crystal boundary segregation
Dragging effect, be remarkably improved recrystallization temperature, the growth rate of ferrite crystal grain is diminished, so organize refined,
The Nb of solid solution suppresses ferritic recrystallization by the mechanism of climbing of the drag mechanism limitation dislocation to solute.Nb（C, N）Tool
There is low solid solubility temperature, it can be achieved that relatively low slab heating temperature, so as to improve yield rate and reduce cost, and relatively low slab
Heating-up temperature, can also reduce the generation of AlN field trashes.Therefore present invention provide that Nb is not less than 0.04%, but the analysis of excessive Nb
Going out thing will be unfavorable to magnetic property, therefore present invention provide that Nb is no more than 0.20%, preferably：The weight percent content of Nb is
0.063-0.185%, further preferably：The weight percent content of Nb is 0.08-0.176%；Accordingly it is dissolved niobium Nb*Content
0.04% ＜ Nb*% ＜ 0.08%.
Why the heating-up temperature of continuous casting billet is set to 1100-1150 DEG C by the present invention, and time inside furnace 2-4h, is because of NbN
And Nb（C, N）With the general characteristic as non-orientation silicon steel inhibitor, it can ensure hot rolling essence with low solid solubility temperature
In the case of degree, slab heating temperature is reduced.Using the roughing of 6-8 times, make crystal grain refinement thick in steel；Control finish rolling at the same time
Inlet temperature ensures that rolling is smooth at 950-990 DEG C.Suitable control finishing temperature is 810-850 DEG C and coiling temperature 650-680
DEG C, driving force on the one hand is provided for the dynamic recovery in steel plate and dynamic recrystallization, is on the other hand improved by precipitation strength
Intensity.Excessive coiling temperature causes Nb（C, N）Disperse educt is unable to, too low coiling temperature is unfavorable to reducing iron loss.Finally
It is 2.10 ± 0.05mm to control hot rolling plate thickness.
840 DEG C -940 DEG C of present invention control normalizing soaking temperature and soaking time 20-60s are necessary conditions.Excessive is normal
It is all unfavorable to improving yield strength to change temperature and excessively slow plate speed, but too low normalizing temperature and too fast plate speed
It is all unfavorable to improving magnetic property.
Cold rolling is to realize the committed step of high thickness and precision.Control cold rolling total reduction to be not less than 80%, and ensure preceding road
It is secondary using big reduction ratio i.e. more than 35%, final pass uses less reduction ratio（5-10%）, make cold change in microscopic structure
Shape tissue increases, and annealing grains are assembled to γ lines, is formed strong { 111 }<112>Texture, the increase of substructure middle position dislocation density.
Continuous annealing is also to realize the committed step of high-performance and high strength bond, 750-820 DEG C of annealing temperature of control and
Soaking time 60-120S, on the one hand will reduce iron loss and improve magnetic strength, another aspect high intensity needs partial annealing, makes steel plate
In there are part non-recrystallization tissue, and retain dislocation caused by cold rolling heavy reduction, it is common with precipitation strength in dislocation strengthening
Under effect, ensure yield strength in more than 600MPa.Annealing atmosphere is pure dry N2, avoid because of H2, moisture etc. oxidation is produced in stove
Reduction reaction, causes furnace roller dross；Last layer half organic coating is applied in surface of steel plate at the same time, prevents from producing larger whirlpool during lamination
Stream loss.
It is contemplated that by add a small amount of Nb and finely tune C, N content and suitable preparation process come produce high intensity and
The non-oriented electrical steel product that high-performance has both, meets high speed rotor of motor steel needs.
The component and preparation process of non-oriented electrical steel of the present invention are mainly around high intensity and high-performance designs.Set in intensity
In terms of meter based on the precipitation strength and solution strengthening of Nb, by technological measures such as process annealings while magnetic property is ensured,
Retain certain dislocation density and improve yield strength；In magnetic property design aspect, ensured necessarily by necessary alloy content
Magnetic property.Meanwhile make full use of inhibitory action and Nb of the Nb to recrystallization（C, N）With low solid solubility temperature, it can be achieved that relatively low
Hot rolling slab heating-up temperature and the technique section for suitably relaxing finished products, reduce production difficulty so as to improve yield rate and reduction
Cost.
Compared with prior art, the present invention end properties of the thickness no more than 0.35mm resist in yield strength >=600MPa
Tensile strength >=700MPa, P1.0/400≤ 35W/kg, B5000≥1.60T。
Brief description of the drawings
Fig. 1 is the metallographic structure figure of silicon steel plate after normalizing of the present invention, it remains the incomplete of part hot rolling deformation tissue
Recrystallization；
Fig. 2 is the metallographic structure figure of production board of the present invention, its incomplete recrystallized tissue adds part cold-rolling deformation tissue.
Embodiment
The present invention is described in detail below：
Table 1 is various embodiments of the present invention and the chemical composition comparative example of comparative example；
Table 2 is various embodiments of the present invention and the main technologic parameters comparative example of comparative example；
Table 3 is the capabilities list of various embodiments of the present invention and comparative example.
Each case study on implementation of the present invention follows the steps below production：
1）Through converter smelting and it is cast into base；
2）Continuous casting billet is heated, control soaking temperature is at 1100-1150 DEG C, time inside furnace 2-4h；
3）Carry out conventional roughing and finish rolling, and after controlling hot rolling plate thickness in 2.10 ± 0.05mm；
4）Normalizing is carried out, control normalizing soaking temperature is at 840-940 DEG C, and soaking time is in 20-60s；
5）Cold rolling is carried out after pickling：Mill product finished product thickness is no more than 0.35mm；
6）Continuous annealing is carried out, and controls soaking temperature for soaking time in 60-120s, atmosphere is pure dry N at 750-820 DEG C2。
1 various embodiments of the present invention of table and comparative example the composition value list（wt%）
Note：Silicon equivalent weight Sieq=Si+2Als-0.5Mn+2.92P is dissolved Nb*%=（Nb/93-C/12-N/14）*100
The main technologic parameters comparative example of 2 various embodiments of the present invention of table and comparative example
The magnetic property and mechanical property list of 3 various embodiments of the present invention of table and comparative example
From table 3 it can be seen that only Composition Control and technological requirement within the scope of the claims, can be produced and met the requirements
Product., excessive, too low normalizing and annealing temperature and time, can be to magnetic property and mechanicalness when component is met the requirements
Different influences can be caused, temperature is crossed high-mechanical property and can not be met the requirements, and the too low magnetic property of temperature can not be met the requirements, and sees pair
Ratio 1,2,3.When technique is met the requirements, the element such as Nb, Si, N is too high or too low, can not reach target call, and Nb is excessive
Then magnetic property is poor, and the too low then mechanical properties of Nb are poor；Si high increases cold rolling difficulty, and the low magnetic properties of Si can not with mechanical performance
Ensure；N it is low because precipitate is few and poor mechanical property, N high then seriously affect magnetic property and can bring magnetic aging, see comparative example 4 ~ 8.
Present embodiment is only the best example, not to the restricted implementation of technical solution of the present invention.
Claims (8)
1. a kind of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels, its chemical composition are by weight percentage：C：
0.001-0.003%, Si：2.6-3.4%, Mn：0.20-0.60%, P≤0.005%, S≤0.005%, Als：0.75-0.95%, N：
0.002-0.006%, Nb：0.053-0.20%, remaining is iron and residual content；And to meet at the same time：4.5%≤Si+2Als-
0.5Mn+2.92P≤5.0%, solid solution niobium Nb*0.04% ＜ Nb of content*% ＜ 0.08%, Nb*%=(Nb/93-C/12-N/14) * 100,
1≤N/C≤3。
A kind of 2. yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1, it is characterised in that：Nb
Weight percent content be 0.063-0.185%.
3. a kind of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1 or 2, its feature exist
In：The weight percent content of Nb is 0.08-0.176%.
A kind of 4. yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1, it is characterised in that：N
Weight percent content be 0.0043-0.0055%.
A kind of 5. yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1, it is characterised in that：Gu
Molten niobium Nb*0.046% ＜ Nb of content*% ＜ 0.073%.
A kind of 6. yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1, it is characterised in that：Control
The ratio of N and C processed are in 1≤N/C≤2.
7. a kind of production method of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels as claimed in claim 1, its
Step：
1）Through converter smelting and it is cast into base；
2）Continuous casting billet is heated, control soaking temperature is at 1100-1150 DEG C, time inside furnace 2-4h；
3）Carry out conventional roughing and finish rolling, and after controlling hot rolling plate thickness in 2.10 ± 0.05mm；
4）Normalizing is carried out, control normalizing soaking temperature is at 840-940 DEG C, and soaking time is in 20-60s；
5）Cold rolling is carried out after pickling：Mill product finished product thickness is no more than 0.35mm；
6）Continuous annealing is carried out, and controls soaking temperature for soaking time in 60-120s, atmosphere is pure dry N at 750-820 DEG C2。
8. a kind of method of yield strength 600Mpa grades of high speed rotor non-orientation silicon steels is produced as claimed in claim 6, its
It is characterized in that：Normalizing soaking temperature is at 860-920 DEG C.
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| CN110616370A (en) * | 2019-08-30 | 2019-12-27 | 武汉钢铁有限公司 | Production method of cold-rolled non-oriented silicon steel with excellent iron loss performance under low field |
| CN114369761A (en) * | 2022-01-07 | 2022-04-19 | 山西太钢不锈钢股份有限公司 | Thin non-oriented silicon steel and preparation method thereof |
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| CN114369761A (en) * | 2022-01-07 | 2022-04-19 | 山西太钢不锈钢股份有限公司 | Thin non-oriented silicon steel and preparation method thereof |
| CN114369761B (en) * | 2022-01-07 | 2022-11-25 | 山西太钢不锈钢股份有限公司 | Thin non-oriented silicon steel and preparation method thereof |
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