CN107964631A - The high speed rotor of motor non-orientation silicon steel and production method of yield strength >=500MPa - Google Patents
The high speed rotor of motor non-orientation silicon steel and production method of yield strength >=500MPa Download PDFInfo
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- CN107964631A CN107964631A CN201711352947.9A CN201711352947A CN107964631A CN 107964631 A CN107964631 A CN 107964631A CN 201711352947 A CN201711352947 A CN 201711352947A CN 107964631 A CN107964631 A CN 107964631A
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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
- C21D8/1222—Hot rolling
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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
- C21D8/1233—Cold rolling
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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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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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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- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
Abstract
The high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa, its chemical composition are calculated as by wt%：Si：2.5~4.5%, Al：0.8~2.0%, Mn：0.5~2.0, N≤0.005%, S≤0.002%, C≤0.003%, P≤0.05%, Cu≤0.05%, Ti+Nb+V+Zr≤0.01%；Production method：Simultaneously RH vacuum refinings after converter smelting；To heating strand；Finish rolling after roughing；Batch；Pickling；Cold rolling；Annealing.Compared with prior art, the present invention in the case where not adding extra alloying element and saving normalizing process, the mechanical strength of non-orientation silicon steel can be effectively improved, its yield strength is not less than 500MPa, is P for 0.35mm and following thickness finished product iron loss1.0/400≤18W/kg。
Description
Technical field
The present invention relates to non-orientation silicon steel and production method, the high speed for particularly belonging to a kind of yield strength >=500MPa is electric
Machine rotor non-orientation silicon steel and its production method.
Background technology
High-speed electric expreess locomotive is often referred to the motor that rotating speed exceedes 10000r/min, its power of motor density is high, small, in new energy
Source automobile, aviation, ship domain have a good application prospect.Especially high-speed permanent magnetic synchronous motor, since its power is close
Degree is high, and size is small, light-weight, and the range of speeds is broad, has a wide range of applications in new-energy automobile field.Permanent magnet synchronous motor turns
Magnetic bridge narrower width in son, some researches show that magnetic bridge width is narrower, permanent-magnet torque and total torque are higher, and electric efficiency is also got over
It is high.And rotor is subject to larger centrifugal stress in high speed rotates, the thinned of magnetic bridge width can cause stress more to be concentrated, in frequency
Rotor easily produces fatigue fracture during numerous speed-changing rotation, and permanent magnet is embedded among rotor.Therefore pacify in view of motor
There is high-yield strength and highly anti-fatigue intensity to resist centrifugal force for full property requirement, electrical sheet.Consider in safety problem, warp
Experimental study, it is believed that the yield strength of orientation free silicon steel plate is suitable in more than 500MPa.
Rotor is exactly iron loss with another index of non-oriented electromagnetic steel sheet.Magnetic fluctuation component in motor focuses primarily upon
Stator core, iron loss are mainly produced by stator core, particularly stator tooth.The change in magnetic flux density in rotor core and permanent magnet
It is smaller, and change in magnetic flux density is larger in stator core.Therefore relative to stator core loss, the loss in rotor and permanent magnet
It can ignore.And from frequency analysis it is contemplated that harmonic component amplitude very little in rotor, the iron loss in stator can be much larger than
Rotor.Therefore the loss that rotor produces does not have too much influence to the efficiency of motor, the material used compared with stator, rotor nothing
The slightly higher iron loss of oriented electrical steel is acceptable.But the fever that rotor is produced when being lost has demagnetization to permanent magnet
Effect, is indirectly degrading the performance of motor, and rotor core radiates increasingly difficult, rotor iron loss for stator core
Height can improve the operating temperature of motor, this service life to bearing and other electronic components brings adverse effect.Therefore to rotor
Cannot be excessive with the iron loss particularly high-frequency loss of non-oriented silicon steel sheet.
In order to suppress the fatigue deformation of magnetic bridge under high speed centrifugation power, magnetic bridge width is difficult to infinitely reduce, additionally, due to silicon steel
Piece magnetic resistance is far below air, and the air-gap flux in iron core is more likely to through magnetic bridge, so as to inevitably cause leakage field, is made forever
Magnet utilization rate reduces, but on the other hand, the torque of permanent magnet synchronous motor also takes full advantage of the reluctance torque of rotor, therefore
Rotor non-oriented electromagnetic steel sheet is to magnetic strength generally without particular/special requirement.
Therefore, high speed rotor of motor non-orientation silicon steel electromagnetic steel plate must possess higher intensity, and iron loss level can be with
Relative loose, but can not be excessive.
Domestic and international Patents documents are consulted, two classes can be divided into according to the method for improving non-orientation silicon steel mechanical strength：
That is precipitation strength and solution strengthening.
Document JP 2011-99163 A propose a kind of manufacture method of high intensity non-orientation silicon steel, its composition characteristic：C:≤
0.02%, Si:1.6-3.0%, Mn:≤1.0%,Al:0.1-3.0%, Ni:≤2.0%,Cu:1.0-3.0%, integrated application Ni's
The precipitation strength effect of Solid solution precipitation and Cu improve mechanical strength.
Document JP 2016-183366 A propose a kind of motor high intensity without whereabouts silicon steel and its manufacture method, its component
Feature：C:≤ 0.01%, Si:0.2-4.0%, Mn:0.05-2.0%,Al: ≤2.5%, Cu:0.5-3.0%, using 400-700 DEG C
Anneal more than 1s below 10min, it is strengthened using the precipitate of Cu.
Document JP2013-44009 A propose a kind of manufacture method of rotor non-orientation silicon steel, its composition characteristic：C:≤
0.01%, Si:1.0-3.0%, Mn:0.05-2.0%,Al:0.1-2.0%, S+As+Nb+Ti+V+Zr+N≤0.018, Ti, Nb,
The carbon nitrogen precipitate of this dvielement of V, Zr is by the recrystallization process of strong inhibition silicon steel, so as to reach crystal grain thinning, improves machinery
The purpose of intensity.
Solution strengthening is carried out by improving Si, Ni content, although finished product magnetism will not deteriorate, on cost of alloy is notable
Rise, and solution strengthening adds the intensity before rolling so that rolling difficulty increases.
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.
Precipitation strength is carried out using Ti, Nb, V, Zr this dvielement, if during C in steel≤0.003%, can not obtain puies forward intensity
High sufficient precipitate, when C content is more than 0.01%, magnetic aging is again notable, makes precipitate easily thick precipitation.If nothing takes
Reach 200 DEG C to the temperature of silicon steel, then generate carbide, iron loss easily deteriorates, and Ti, Nb, V, the precipitate strong inhibition of Zr
Recrystallization, iron loss deteriorate serious.
Therefore, the alloy and production cost of non-orientation silicon steel how are reduced, obtains ensureing while higher mechanical strength
Certain iron loss, becomes current rotor non-orientation silicon steel urgent problem to be solved.
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 0.35mm and following thickness, surrender
Intensity is in more than 500MPa, iron loss P1.0/400The high speed rotor of motor non-orientation silicon steel and production method of≤18W/kg.
Realize the measure of above-mentioned purpose：
The high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa, its chemical composition are by weight percentage：Si：
2.5~4.5%, Al：0.8~2.0%, Mn：0.5~2.0, N≤0.005%, S≤0.002%, C≤0.003%, P≤0.05%, Cu
≤ 0.05%, Ti+Nb+V+Zr≤0.01%, other is Fe and inevitable impurity.
Preferably：The weight percent content of Si is 3.0~4.0%.
Preferably：The weight percent content of Al is 1.0~1.6%.
Preferably：The weight percent content of Mn is in .8~1.5%.
The method for producing the high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa, its step：
1）After converter smelting and carry out RH vacuum refinings；
2）It is casting continuously to form after base to heating strand, for heating-up temperature at 1000~1200 DEG C, heating time is not less than 100min；
3) finish rolling is carried out after conventional roughing, and controls finish rolling finishing temperature to meet：
650 DEG C≤finishing temperature≤[650+（Si+Al）×50]℃；
In formula：Si and Al is the weight percent content set in steel plate and is calculated according to the data of percentage by weight；
4）Batched, coiling temperature is 500~600 DEG C；
5）Carry out conventional pickling；
6）Cold rolling is carried out, the finished product thickness no more than 0.35mm is rolling to using once cold rolling method；
7) to anneal, annealing temperature is heated under the conditions of firing rate is 40~100 DEG C/s, annealing temperature is 600~700 DEG C,
Soaking time is 1.5-3min.
Preferably：Slab heating temperature is at 1025~1150 DEG C.
Preferably：Finish rolling finishing temperature meets:750 DEG C≤finishing temperature≤815；
Preferably：Step 7）In annealing heating rate in 50~88 DEG C/s.
The effect of each element in the present invention
(1)C:≤0.003%
C can cause magnetic aging, can also form TiC, make magnetic variation, therefore reduce its content as far as possible.
(2)Si:2.5~4.5%
Si is the element for improving steel plate resistivity, so that iron loss is reduced, therefore Si contents need to be more than 2.5%, and when the additive amount of silicon
When excessive, embrittlement, which can occur, for steel plate causes rolling difficult, therefore Si upper content limits are arranged to 4.5%.Its further preferred content
Si:3.0~4.0%.
(3) Al:0.8~2.0%
The aluminium of solid solution can substantially reduce the eddy-current loss of steel by ferritic resistivity is improved, in high frequency eddy current losses ratio
Total losses can be significantly reduced in the case of larger, therefore Al content needs to be more than 0.5%, but Al can substantially reduce saturation magnetic strength
Bs, the brittle influence on steel plate is also big, easily produces internal oxidition in annealing, therefore the Al content upper limit is set as 2.0%.Into
One step preferably its content Al:1.0~1.6%.
(4)Mn:0.5~2.0%
Mn can improve hot rolling plasticity, make the increase of steel plate hardness, improve steel plate punching, and during Mn≤0.5%, iron loss cannot be abundant
Reduce, form tiny precipitate iron loss increase.And during Mn >=2.0%, the carbide of Mn largely forms and iron loss can be caused to increase.Into
One step preferably its content Mn:0.8~1.5%.
(5)S:≤0.002%
S can cause the precipitation of MnS, TiS, CuS, hinder crystal grain to grow up, make magnetic variation.
(6)N:≤0.003%
N can cause the precipitation of AlN, TiN, crystal grain is grown up and be obstructed, therefore its content is below 0.003%.
(7)P:0.005~0.05%
P can improve resistivity, can also improve armor plate strength, improve punching, therefore set it to more than 0.005%.But
P content can make steel plate brittle, increase production risk more than 0.05%.
(8)Cu:≤0.05%
Cu unessential elements, can form tiny sulfide makes magnetic deterioration, therefore Cu contents are more low better.
(9)Ti+Nb+V+Zr:≤0.01%
Ti, Nb, V, Zr are carbide and nitride forming element, its precipitate can effectively suppress the recrystallization of steel plate, are improved
Dislocation density, crystal grain thinning, so as to improve the intensity of steel plate, but plays precipitate and is suppressing the recrystallization of steel plate, crystal grain thinning
While can severe exacerbation steel plate magnetic property, especially cause manufacture rotor non-orientation silicon steel iron loss be substantially increased, generate heat
Seriously.Therefore Ti+Nb+V+Zr is limited to less than 0.01%, preferably Ti+Nb+V+Zr≤0.005%.
Secondly, the effect to texture in the present invention illustrates.
The iron monocrystal body of body-centered cubic crystallographic system<111>Direction is atom solid matter direction, its elasticity modulus（Intensity）Maximum,
For 248GPa, and<100>Direction atomic density is minimum, its elasticity modulus is also minimum, is 165GPa, the elasticity modulus of main crystal orientation
See attached drawing 1.
From the perspective of intensity is improved, it is desirable to which the crystal face of material includes as far as possible<111>Etc. crystal orientation, do not include at the same time<
100>Etc. crystal orientation.Such as { 211 }, { 321 }, { 431 }, { 110 } crystal face all include<111>Crystal orientation, still { 110 } crystal face include<
001>Crystal orientation.Therefore final to wish to improve { 211 }, { 321 }, { 431 } crystal face component intensity is to improve finished product mechanical performance.And
{ 100 } plane texture includes<001>,<010>,<310>,<210>Etc. crystal orientation, therefore it should try one's best and reduce its component intensity.
Each production technology of silicon steel can all have an impact finished product texture, such as the raising with finishing temperature, after hot rolling again
Crystallization is easier, and recrystallization rate is also higher, and hot rolled plate { 100 } plane texture has strengthened, and { 110 } and { 111 } plane texture is strong at the same time
Degree has weakened.Normalizing can make hot rolled plate tissue evenly after hot rolling, and recrystal grain increases, and strengthen { 100 } and { 110 } group
Point, weaken { 111 }, { 211 }, { 321 }, { 431 } plane texture.It is mechanical strong so as to improve in order to preferably optimize the component of texture
Degree, defines texture strengthening factor Is here
Is values are bigger, and the contribution to mechanical strength is bigger, and the mechanical strength of material is also higher.Furthermore, it is contemplated that texture is to finished product
Magnetism also has certain influence, { 211 }, { 321 }, and the texture such as { 431 } is unfavorable to iron loss, and the texture such as { 100 }, { 110 } is to iron loss
Favorably, therefore the bigger adverse effect to iron loss of Is values is more serious.
Consider texture strengthening factor Is to mechanical strength and magnetic influence, present invention provide that Is scopes 1.0 ~
2.0, preferably Is scopes are in 1.3-1.8.
The effect of master operation in the present invention
（1）With the raising of hot rolling finishing temperature, it is easier to be recrystallized after hot rolling, and recrystallization rate is also higher, hot rolled plate { 100 } face
Texture has strengthened, and { 110 } and { 111 } plane texture intensity has weakened at the same time.Finishing temperature is too low, and crystal grain is excessively tiny, if
Without normalizing, rolling load is excessive when can cause cold rolling, and the easy brittle failure of steel plate, finishing temperature is excessive, and crystal grain is excessively thick,
{ 100 } plane texture has strengthened, it is contemplated that finished product { 100 } plane texture is too strong after the inheritance of texture can cause annealing, reduces into
Product intensity.Therefore, hot rolling finishing temperature scope is defined as：650 DEG C≤finishing temperature≤[650+（Si+Al）× 50] DEG C, more
Further preferred finishing temperature：750-815℃.
（2）When hot-rolling coiling temperature is less than 500 DEG C, sample upper and lower surface is recrystallized structure, and middle part lacks recrystallization and drives
Power, without recrystallized structure, solute atoms is difficult to happen effective diffusion over long distances in a short time, is formed to easy disperse
The precipitates such as AlN, the pinning crystal boundary after cold rolled annealed, finished product iron loss deteriorates after causing annealing.When coiling temperature is more than 600 DEG C
When, microstructure is there are growing up after Static Recrystallization, while dissolving and the diffusion of solute atoms including tiny precipitate, in
Portion's recrystallized structure increases, and fiber band is reduced, { 111 }, { 211 }, { 321 }, and the texture such as { 431 } is reduced, it is contemplated that texture after
Holding property can cause after annealing { 211 }, and { 321 }, { 431 } plane texture dies down, and reduce product intensity.Therefore, by hot-rolling coiling temperature
Scope is defined as：500-600℃.
（3）Normalizing process is eliminated after hot rolling, because normalizing can make hot rolled plate tissue evenly after hot rolling, recrystallization is brilliant
Grain increases, and strengthens { 100 } and { 110 } component, weakens { 111 }, { 211 }, { 321 }, { 431 } plane texture.In view of texture after
Finished product { 100 } plane texture is too strong after holding property can cause annealing, { 211 }, { 321 }, and { 431 } plane texture dies down, and reduces product intensity.
（4）Finished products：40 DEG C/s≤firing rate≤100 DEG C/s.Annealing heating rate's finished product texture has very high point
It is, under the conditions of high firing rate, goss texture { 110 } in the initial coarse grain sample of hot rolling<001>Component significantly increases, { 111 },
{ 211 }, { 321 }, { 431 } texture slightly weaken, although goss texture intensity reduces in the initial fine grain sample of hot rolling, at the same time
{ 111 }, the texture such as { 211 }, { 321 }, { 431 } is greatly lowered.And under the conditions of low firing rate, the initial coarse grain examination of hot rolling
Weaker { 110 } component becomes strong in sample, and the goss texture intensity that the initial fine grain sample of hot rolling is corresponded in finished product reduces,
{ 111 }, the texture component intensity such as { 211 }, { 321 }, { 431 } increase substantially.Reason is that the forming core of Gauss orientation crystal grain leads to
Often occur, in annealing early stage, there is the chance more grown up, but the reply occurred under the conditions of low firing rate is stronger, then tie
Before crystalline substance starts, the difference of remaining energy storage weakens between each texture component, therefore the chance grown up of Gauss crystal grain is reduced, while again
Crystallize early stage Main Texture component { 111 }, { 211 }, { 321 }, { 431 } nucleus component by consume around deformed matrix and
Grown up.In the present invention when hot rolling finishing temperature is relatively low, and cancels normalizing process, hot rolled plate crystal grain is smaller, when annealing adds
When thermal velocity is more than 100 DEG C/s, the goss texture intensity that the initial fine grain sample of hot rolling is corresponded in finished product improves, { 111 },
{ 211 }, the texture component such as { 321 }, { 431 } intensity significantly declines, and is unfavorable for the raising of product intensity, but when annealing heating speed
Degree is when being less than 40 DEG C/s, goss texture remitted its fury, { 111 }, { 211 }, { 321 }, and the texture component intensity such as { 431 } significantly carries
Height, can cause iron loss to be greatly lowered, therefore after meeting hot rolling finishing temperature and cancelling normalizing process, finished products heating speed
Degree should control 40-100 DEG C/s, still more preferably firing rate：50-88℃/s.
Compared with prior art, the present invention do not adding extra alloying element, and in the case of saving normalizing process, can have
Effect improves the mechanical strength of non-orientation silicon steel, its yield strength is in more than 500MPa, for 0.35mm and following thickness finished iron
Damage as P1.0/400≤18W/kg。
Brief description of the drawings
Attached drawing 1 is the elasticity modulus schematic diagram of main crystal orientation in body-centered cubic crystallographic system of the present invention.
Embodiment
The present invention is described in detail below：
Various embodiments of the present invention are produced according to following steps：
1）After converter smelting and carry out RH vacuum refinings；
2）It is casting continuously to form after base to heating strand, for heating-up temperature at 1000~1200 DEG C, heating time is not less than 100min；
3）Finish rolling is carried out after conventional roughing, and controls finish rolling finishing temperature to meet：
600 DEG C≤finishing temperature≤[650+（Si+Al）×50]℃；
In formula：Si and Al is the weight percent content set in steel plate and is calculated according to the data of percentage by weight；
4）Batched, coiling temperature is 500~600 DEG C；
5）Carry out conventional pickling；
6）Cold rolling is carried out, 0.35mm and following finished product thickness are rolling to using once cold rolling method；
7) anneal, annealing temperature is heated under the conditions of firing rate is 40~100 DEG C/s, annealing temperature is 600~700 DEG C.
Embodiment
Using converter smelting, the specific component for testing steel is shown in Table 1, carries out RH application of vacuum, be casting continuously to form base.Strand is added
Heat, then carries out roughing, and finish rolling, is batched, and normalizing or directly carries out pickling after hot rolling, 0.35mm is once cold rolled to after pickling.It is right
Cold-reduced sheet carries out finished products, and concrete technology is shown in Table 2.It is as shown in table 3 that finished product corresponds to the texture strengthening factor, performance.
The comparative example of 1 various embodiments of the present invention of table and comparative example（wt%）
Each component example of the present invention of table 2 corresponds to technique list
Each component example corresponding performance list of the present invention of table 3
As can be seen from the above embodiments, only when chemical composition meets claim, and hot rolling finishing temperature meet 600 DEG C≤
Finishing temperature≤[650+（Si+Al）× 50] DEG C, coiling temperature does not use normalizing process, annealing heating rate at 500-600 DEG C
Reach target, material in 40-100 DEG C/s, 600-700 DEG C of annealing temperature, soaking time 1.5-3min, the texture strengthening factor of material
The mechanical performance and iron loss of material could meet target call at the same time.Use preferred component and technique, the mechanical performance of material at the same time
Can be more excellent with iron loss.
Above-described embodiment is only the best example, and is not the restriction to embodiments of the present invention.
Claims (8)
1. the high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa, its chemical composition are by weight percentage：
Si：2.5~4.5%, Al：0.8~2.0%, Mn：0.5~2.0, N≤0.005%, S≤0.002%, C≤0.003%, P≤0.05%,
Cu≤0.05%, Ti+Nb+V+Zr≤0.01%, other neither block the impurity avoided for Fe.
2. the high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa as claimed in claim 1, it is characterised in that：
The weight percent content of Si is 3.0~4.0%.
3. the high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa as claimed in claim 1, it is characterised in that：
The weight percent content of Al is 1.0~1.6%.
4. the high speed rotor of motor non-orientation silicon steel of yield strength >=500MPa as claimed in claim 1, it is characterised in that：
The weight percent content of Mn is in .8~1.5%.
5. the method for the high speed rotor of motor non-orientation silicon steel of production yield strength >=500MPa as claimed in claim 1,
Its step：
1）After converter smelting and carry out RH vacuum refinings；
2）It is casting continuously to form after base to heating strand, for heating-up temperature at 1000~1200 DEG C, heating time is not less than 100min；
3) finish rolling is carried out after conventional roughing, and controls finish rolling finishing temperature to meet：
650 DEG C≤finishing temperature≤[650+（Si+Al）×50]℃；
In formula：Si and Al is the weight percent content set in steel plate and is calculated according to the data of percentage by weight；
4）Batched, coiling temperature is 500~600 DEG C；
5）Carry out conventional pickling；
6）Cold rolling is carried out, is rolling to using once cold rolling method no more than the finished product thickness in 0.35mm；
7) to anneal, annealing temperature is heated under the conditions of firing rate is 40~100 DEG C/s, annealing temperature is 600~700 DEG C,
Soaking time is 1.5-3min.
6. the method for the high speed rotor of motor non-orientation silicon steel of production yield strength >=500MPa as claimed in claim 5,
It is characterized in that：Slab heating temperature is at 1025~1160 DEG C.
7. the method for the high speed rotor of motor non-orientation silicon steel of production yield strength >=500MPa as claimed in claim 5,
It is characterized in that：Step 3）In finish rolling finishing temperature meet 750 DEG C≤finishing temperature≤815 DEG C.
8. the method for the high speed rotor of motor non-orientation silicon steel of production yield strength >=500MPa as claimed in claim 5,
It is characterized in that：Step 7）In annealing heating rate in 50~88 DEG C/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711352947.9A CN107964631B (en) | 2017-12-15 | 2017-12-15 | Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711352947.9A CN107964631B (en) | 2017-12-15 | 2017-12-15 | Non-oriented silicon steel with yield strength of more than or equal to 500MPa for high-speed motor rotor and production method |
Publications (2)
| Publication Number | Publication Date |
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| CN107964631A true CN107964631A (en) | 2018-04-27 |
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