CN1888112A - High magnetic induction and high grad non-orientation electrical steel and its making process - Google Patents
High magnetic induction and high grad non-orientation electrical steel and its making process Download PDFInfo
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- CN1888112A CN1888112A CN 200510027401 CN200510027401A CN1888112A CN 1888112 A CN1888112 A CN 1888112A CN 200510027401 CN200510027401 CN 200510027401 CN 200510027401 A CN200510027401 A CN 200510027401A CN 1888112 A CN1888112 A CN 1888112A
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The present invention is high magnetic induction and high grade non-orientation electrical steel and its making process. The high magnetic induction and high grade non-orientation electrical steel consists of C not more than 0.0050 wt%, N not more than 0.0030 wt%, Si 1.50-2.50 wt%, Al 0.80-1.30 wt%, Mn 0.20-0.50 wt%, P not more than 0.030 wt%, S not more than 0.005 wt%, Sb 0.03-0.10 wt% or Sn 0.05- 0.12 wt%, and B 0.0005-0.0040 wt%, except Fe and inevitable impurities. Its making process includes initial rolling and high temperature winding to obtain ideal hot rolled steel belt structure; cold rolling to provide the energy for crystal grain growth in re-crystallizing annealing, and re-crystallizing annealing in controlled temperature to obtain ideal crystal grain structure. It has excellent surface quality, high magnetic induction and low iron loss, and is suitable for use in high efficiency motor iron core.
Description
Technical field
The present invention relates to non-oriented electrical steel and manufacture method thereof, particularly product mainly is the manufacturing process as the high grade non-oriented electrical steel with high magnetic strength of producing high efficiency motor iron core.
Background technology
Conventional method for production of non-oriented electrical steel utilizes silicon (Si) can improve the characteristic of ferrous materials resistivity, realize reducing the purpose of iron loss by adding silicon, but the decline that has brought magnetic conductivity owing to the rising of resistivity simultaneously finally causes the reduction of magnetic strength. So, adopt the high grade non-oriented electrical steel (high Si content) of conventional production method manufacturing although can obtain lower iron loss to a certain extent, also exist magnetic strength to hang down drawback simultaneously. Current take energy savings, raise the efficiency the electromechanics trade as developing direction, require its main material---non-oriented electrical steel---when having low iron loss, also will have high magnetic strength, this has just proposed challenge to conventional high grade non-oriented electrical steel production method.
The present invention is from improving the mechanism of electrical steel product magnetic strength, pass through adjusting component, raising Al content substitutes the effect of Si, reach the purpose that reduces iron loss, coming Substitute For Partial Si with Al simultaneously also is in order to obtain more (100) cubic texture, to reduce because the anisotropy that high Si brings; Add segregation element Sn, Sb etc., obtain desirable texture, thereby improve magnetic strength; For eliminate low-carbon (LC) (＜50ppm) in the situation, because high Si+Al (＞2%) caused ' corrugated defective ', require hot rolling roughing≤4 passages, roughing accumulative total reduction ratio 〉=80%, wherein has the reduction ratio of a passage 〉=40% at least, the roughing rolling technique that the high rolled form factor of the reduction ratio of 2 above passages 〉=40% is preferably arranged, purpose are (100) column crystals that destroys as-cast structure, improve recrystallization isometry rate; Finish-rolling process and annealing process also are optimized, reasonable distribution percentage pass reduction, the control rate of heat addition etc., suppress simultaneously to be difficult for magnetized (111) γ texture in desirable easily magnetized (100) the α texture of acquisition, and obtain desirable grain structure, thereby when obtaining low iron loss, also improve largely magnetic strength, keeping low iron loss (P15/50＜magnetic strength B 2.3W/Kg) time50Improve (B more than 0.05 tesla than conventional method50＞1.71Tesla, 0.35mm). Because the adding of Sb/Sn may cause embrittlement of grain boundaries, the present invention has added suitable B and has played the effect of strengthening crystal boundary, can prevent the broken belt in the operation of rolling in order to offset. Simultaneously in order to improve the cold-workability of the large production of high Si steel band, the present invention utilizes aluminium also to have the characteristic of raising resistivity and little impact processing, by adding Al Substitute For Partial Si, but reach the purpose of continuous rolling in the cold rolling production, enhance productivity, this also becomes possibility so that increase cold rolling reduction ratio (＞84%), reaches to reduce the anisotropic purpose of final finished, is conducive to improve the efficient of motor. Smelt the elements such as C and N because the present invention passes through control simultaneously, thereby can omit last decarburizing annealing operation, also can reach the deteriorated effect of control timeliness.
In the past when producing the non-oriented electrical steel of high magnetic strength; 95119969.2), the secondary cold-rolling+intermediate annealing method (patent No.: 91107594.1), control hot rolling rhythm and coiling temperature (patent No.: 11-172333[JP 11172333 A]), two-phase section finish to gauge+high temperature coiling and the thermal-insulating method (patent No.: 95194275.1), high Si hot-strip normalizing method+secondary cold-rolling method (patent No.: 00133842.0), high Mn+ high temperature coiling and the flat 11-172333 of thermal-insulating method (Te Open) etc. can both reach the purpose that improves the electrical steel product electromagnetic performance adopt to increase the intermediate billet temperature retaining of course of hot rolling and the secondary cold-rolling method (patent No.:; but these methods all affect batch production rhythm to a certain extent; increased production process; thereby increased production cost; and patent 95194275.1 adopted the method in two-phase section finish to gauge, so that the stable control ratio of hot rolling difficulty. The patent No. is in 00115993.3 the invention, and the composition system that has adopted high Si+Al and adjusted P+Sn/Sb reaches the purpose of improving electromagnetic performance; But the adding of high Si and high Al and the thick column crystal of slab that adopts destruction to cause thus produce ' corrugated ' defective in final finished easily, and so that the pile pieces coefficient of final products increases, have increased the loss of electric machine and reduced electric efficiency. So this invention has adopted the way that Hot Rolled Plate Normalizing is processed or slow cooling is processed to play the purpose of elimination ' corrugated ' defective, this has increased production process, also will transform on a large scale equipment, so that production cost increases. And patent 01138224.4 has adopted the composition system of low Al, also reaches the effect that improves texture by adjusting P+Sn/Sb; But because the adding of this patent P+Sn/Sb is so that grain-boundary strength is deteriorated rapidly, and do not add intercrystalline strengthening element (such as B) as remedying, so that broken belt very easily in the cold-rolled process, this has increased large production cost virtually. The low temperature casting method (examined patent publication 49-39526 communique) of employing is also arranged in casting process, the cooling of not spraying water in 1～7 second after finish to gauge and the hot rolling more than 1000 ℃, and batch (No. 54023 communiques of examined patent publication 62-) etc. at＜700 ℃ and eliminate production high grade electrical steel product ' corrugated ' defective. But when adopting the low temperature casting method, the liquid steel temperature in the casting process is wayward, and field trash is difficult for come-up in the crystallizer, and the amount of inclusions increases in the continuous casting billet, affects end product quality; Adopt high temperature finish rolling method (examined patent publication 62-54023 communique) to require continuous blank heating temperature to be increased to more than 1250 ℃, easily cause the continuous casting billet waist that collapses, and affect rhythm of production, improved production cost.
Summary of the invention
The object of the invention is to by effective adjustment alloying component, suitably add segregation element, and adopt roughing to depress greatly and destroy slab columanar structure, promote columanar structure to occur that thereby recrystallization is eliminated because ' corrugated ' defective that low C, high Si+Al bring, it is good and have a high grade non-oriented electrical steel of high magnetic strength namely can to obtain surface quality by the once cold rolling method. Production need not normalizing, and iron loss level in kind reaches or is better than the H7 of Nippon Steel～H14 level, and magnetic strength improves more than 500 Gausses than conventional products; Also can further improve the product electromagnetic performance by normalizing process, iron loss further reduces, magnetic strength further improves. Product of the present invention satisfies the requirement of used for high efficiency motor iron core steel fully, also can be used in conventional electric machine iron core, can improve electric efficiency, improves operating index, realize saving energy and reduce the cost.
Technical scheme of the present invention is,
The present invention at first starts with from optimizing the high grade non-oriented electrical steel composition, obtain low iron loss by silicon (1.5～2.5%) and aluminium (0.8～1.3%), obtain simultaneously preferably machinability, and make Second Phase Precipitation thing (such as AlN etc.) alligatoring; It is deteriorated that control C content＜30ppm eliminates the timeliness of electromagnetic performance; Rationally add suitable segregation element Sb (0.05%～0.10%) or Sn (0.08%～0.12%), control B/N＜4.0, design novel alloy system, final more easy magnetization (100) α texture and inhibition (111) γ texture of obtaining reduces iron loss, improves magnetic strength; Depress greatly the purpose that the thick column crystals of destruction such as rolling and matte roll is rolling reach elimination " corrugated " defective by the roughing passage; Make Second Phase Precipitation thing (such as AlN, MnS etc.) alligatoring, optimize each percentage pass reduction and obtain desirable hot-strip tissue by high temperature coiling, also obtain desirable texture; By adjusting the hot rolling pass reduction ratio, improving cold rolling reduction ratio, obtain (100) α texture of more easy magnetization and suppress (111) γ texture, alleviate because the anisotropy that the adding of Si causes raises, reduce the loss of motor when operation, simultaneously also can be by improving cold rolling reduction ratio, for grain growth in the final recrystallization annealing process provides larger energy (deformation energy); Obtain the desirable measures such as grain structure by control recrystallization annealing temperature, obtain being applicable to high efficiency motor iron core, also being applicable to the high grade non-oriented electrical steel of common electric machine iron core of the high magnetic strength of having of excellent surface quality, low iron loss. Also can pass through the hot-strip normalizing process, further obtain to have the electrical sheet of more superior electromagnetic performance.
Its Composition Design scheme is as follows:
C: for non-oriented electrical steel, C content is controlled at below 0.005%, and is best below 0.003%, decarbonization process can be removed from and just the purpose that prevents timeliness can be reached, prevent internal oxidation layer and interior nitration case, reach the purpose that reduces iron loss, can prevent that also hearth roll is stained with iron scale and causes scuffing. Reduce C content, phase transition temperature is raise, be conducive to improve final finished and anneal to obtain desirable tissue, the AlN solid solubility reduces simultaneously, can prevent that tiny AlN from separating out, and can reach the purpose that improves the finished product magnetic strength.
N:N is easy to form tiny AlN particle inhibiting grain growth, so the N content that reduces in the steel is conducive to suppress the formation of tiny AlN particle, thereby improves magnetic strength, reduction iron loss. Simultaneously, N is larger on the impact of timeliness than C, reduces N content, can reduce the impact that magnetic aging brings. In principle N content more low better (best≤as 15ppm), but to consider steel-making cost and actual operability, N content should≤30ppm.
Si: the Si increased content in the steel, the electricalresistivityρ increases, and the iron loss of steel band reduces, but magnetic strength also reduces simultaneously. Because Si increases, also can bring work brittleness to strengthen simultaneously, cause cold rolling difficulty. The present invention is by great many of experiments, finds that the effect that reaches the reduction iron loss by increasing Si content is not very good under Si content reaches situation 2.0% or more. Descend in order to control magnetic strength on the basis that guarantees the reduction iron loss, and guarantee cold rolling machinability, Si content is controlled at≤2.5% (best 1.5%～2.5%).
Al:Al is the same with Si, improve steel resistivity, dwindle the γ phase region, promote grain growth, reduce iron loss, during especially high Al content, promote thick AlN to form, improve texture, reduce iron loss and anisotropy, and fixed nitrogen, magnetic aging is reduced. Al compares with Si in addition, and Al is obvious not as silicon on the impact of the intensity of steel, hardness and ductility, thereby has improved the cold rolling performance of steel. For steel of the present invention, effect the best when Al content is 0.80%～1.30% in the steel when Al content is lower than 0.80% in the steel, in the situation that keeps Si content≤2.5%, is unfavorable for obtaining very low iron loss; When Al content was higher than 1.30% in the steel, molten steel viscosity was excessive, and what impact was cast normally carries out, even caused the nozzle blocking cutout, and the while also brings impact to the welding of cold rolling process band steel. Therefore control Al content 0.80%～1.30%.
Mn:Mn and S form MnS, can prevent from forming the caused hot-short phenomenon of low-melting FeS along crystal boundary, can improve hot rolling plasticity by guaranteeing a certain amount of Mn, simultaneously MnS is lower in the solid solubility of γ in mutually, can impel thickization of MnS, be conducive to later grain growth. The present invention requires Mn/S 〉=10, guarantees good hot-workability and impels thickization of MnS, and cooperate other alloys can improve the punching performance. But because the present invention requires S content low, so Mn content also should not be too high, prevent that hot-strip from separating out tiny MnSiN in preannealing (normalizing) process2 And Mn enlarges γ phase element, when the Mn too high levels, and A3The point phase point temperature is excessively low, causes hot rolling finishing temperature and finished products temperature excessively low, and the finished steel plate crystallite dimension is too small, and is unfavorable to magnetic, but also raises the cost. In conjunction with experimental result, Mn content of the present invention is defined as 0.2～0.5 %.
P:P is larger to the embrittling effect of non-oriented electrical steel steel band, and along with the rising of Si+Al content, this embrittling effect is stronger; Be lower than at C content in the situation of 80ppm, P strengthens along Grain Boundary Segregation, and the grain growth when causing final annealing is obstructed, and { basis of 110} texture evolution has promoted that { the 222} texture evolution causes magnetic strength to reduce in obstruction; Mn promotes again P to Grain Boundary Segregation, and the number of bends of steel band is sharply reduced, and P also damages the cold rolling performance of steel band simultaneously. For high grade non-oriented electrical steel, P should be controlled at≤and 0.040%.
S:S is very large on the electromagnetic performance impact of non-oriented electrical steel, and especially in the situation of high Si+Al, high S can increase substantially iron loss; When S and Mn form tiny MnS, the grain growth in the time of can strongly hindering finished products, magnetic strength significantly descends, iron loss increases substantially. The present invention reaches the purpose that the tiny AlN of abundant control and MnS separate out by high Al, low S. S content is more low better in the steel in principle, but from the angle of steel-making cost and operability, the S content in the steel should be controlled at below the 50ppm.
Sb:Sb is surface active element, can be along crystal boundary and surface segregation, the surface energy of different directions optionally reduces, hinder (hkl) crystal grain along the development of rolling direction, (111) crystal grain obviously reduces, promoted simultaneously the development of (100) texture, can significantly improve the texture of hot rolled plate and production board, the effect that finally reach further reduction iron loss, improves magnetic strength. In containing manganese steel, add Sb and can also stop the hot rolled plate surface to increase N and Si, Al oxidation and nitrogenize, namely can prevent internal oxidation layer and in be nitrided into formation, improve magnetic strength, reduce iron loss. But when Sb content greater than 0.10% the time, too much along the Sb of Grain Boundary Segregation, hinder grain growth, hot rolled plate and production board crystal grain are tiny, iron loss increases, too much Sb can cause grain-boundary weakness, is prone to belt phenomenon in the operation of rolling; When Sb content less than 0.03% the time, very few along the Sb of Grain Boundary Segregation, suppressing crystal boundary (111) crystal grain, to give birth to nuclear capability not enough, do not have enough advantageous effects. Therefore the control range of Sb content is 0.03%～0.10%.
Sn:Sn also is surface active element, can be along crystal boundary and belt steel surface segregation, and the surface segregation degree is stronger than cyrystal boundary segregation. In the recrystallization stage, because the Sn atom is segregated in crystal boundary and belt steel surface, can reduces oxidation in the band steel top layer, prevent that active oxygen from permeating to steel matrix along crystal boundary; Surface energy can optionally reduce and the increased activity of some crystal boundaries, by an amount of Sn content, can obtain more satisfactory belt steel surface texture, (111) crystal grain is inhibited, and can promote the development of favorable texture (100), improve electromagnetic performance. Among the present invention, regulation Sn content 0.05～0.12%, then too much along Grain Boundary Segregation if content is too much, the growing up of crystal grain when hindering final annealing also can increase the risk of operation of rolling band of discontinuance simultaneously; If cross lowly, then can not give full play to the effect that Sn improves texture.
B:B γ mutually in, the preferential combination with N generates BN, separates out thick AlN take BN as core, separates out tiny AlN when organizing hot rolling, makes the damaging effect minimizing of AlN; In addition, B can segregation in course of hot rolling can prevent in the steel because the embrittling effect that the Grain Boundary Segregations such as interpolation Sb or Sn produce at crystal boundary. But when B/N＞4.0, because the B segregation is in crystal boundary, so that (111) component is strengthened, (100) component is inhibited simultaneously, affects the electromagnetic performance of final finished; When the B addition is lower than 0.0005%, do not have favourable effect yet. Therefore, the control range of B content is 0.0005%～0.0040% in the present invention.
Technical scheme of the present invention is: the high grade non-oriented electrical steel plate with low iron loss, high magnetic strength, component comprises: Fe, Si, Al, Mn, P, Sb/Sn, B, C, N, S etc., wherein Sb and Sn selection is wherein a kind of, and the percentage by weight of component is:
C：≤0.0050％
N：≤0.0030％
Si：1.50％～2.50％
Al：0.80％～1.30％
Mn：0.20％～0.50％
P：≤0.030％
S：≤0.005％
Sb：0.03％～0.10％
Sn：0.05％～0.12％
B：0.0005％～0.0040％
All the other are iron and inevitably are mingled with.
Proportioning to the component of non-oriented electromagnetic steel sheet is further optimized, and the ratio range that obtains after preferred is:
C：≤0.0030％
N：≤0.0015％
Si：1.80％～2.20％
Al：0.80％～1.20％
Mn：0.30％～0.50％
P：≤0.030％
S：≤0.003％
Sb：0.05％～0.10％
Sn：0.06％～0.11％
B：0.0005％～0.0030％
All the other are iron and inevitably are mingled with.
Secondly, adopt low-temperature heat technique, 1100～1200 ℃ of slab heating temperatures reduce the solid solution capacity of AlN in heating process, thereby reduce separating out of tiny AlN.
Again, optimize hot rolling technology, especially optimize roughing technique, require roughing≤4 passages, roughing accumulative total reduction ratio 〉=80% wherein has the reduction ratio of a passage 〉=40% at least, the reduction ratio of 2 above passages 〉=40% is preferably arranged, i.e. so-called high rolled form factor (m=2 (Hi-1-H
i)
1/2/(H
i-1+H
i), H whereini-1Thickness, H for the rolling front spring feed mill of i passageiGo out the thickness of milling train for the rolling rear steel plate of i passage) the roughing rolling technique, purpose is to destroy (100) column crystal of as-cast structure, improves recrystallization isometry rate. As everyone knows, in rough rolling process, adopt passage to depress greatly, can reduce the roughing passage, shorten the roughing time, reduce frequency of exposure and time between steel plate and the roll, thereby the temperature drop of minimizing rough rolling process, guarantee that the rough rolling plate blank temperature is at recrystallization critical-temperature (TCr) more than be to obtain high recrystallization rate, the most important condition of high isometry rate tissue. Secondly the stacking fault energy of the ferrous alloy of bcc structure is higher, when the deformation work of unit interval hangs down, not only the inner deformation storage of alloy can be low, and deformation Substructure such as dislocation are easy to climb and the Recovery Process such as slippage are handed in hot activation, dislocation density is reduced rapidly, deformation stores can very fast release, and the recrystallization driving force reduces rapidly, hinders recrystallization and occurs; And deformation Substructure density reduces rapidly, and the recrystallization nucleus reduces greatly at the deformation Substructure nucleation probability, and main forming core on Grain and sub-grain boundary, and grows up rapidly, causes the tissue odds that organizes recrystallization not exclusively to reach recrystallization occurs even. Adopt passage to depress greatly rolling (being that high rolled form factor is rolling), because speed of deformation increases (speed of deformation WhereinFor speed of deformation, Δ h are that the i passage is that absolute draft amount, H are i passage front spring thickness), the deformation work of unit interval increases, unit interval steel plate deformation in the steel plate stores and can increase, to destroy column crystal, obtain an essential condition of high recrystallization rate, high isometry rate tissue, simultaneously also be destroy original (100) column crystal position to essential condition. On the deformation mode: percentage pass reduction is large, be conducive to increase the frictional force of roll and surface of steel plate, cause that the steel plate shearing deformation quantity increases, shearing deformation increases along the steel plate thickness Directional Penetration Depth, rollingly change complicated strain regime into by plane strain state, the lattice rotation degree of crook is large, and deformation stores can be high, destroy columanar structure's effect and increase, promote columanar structure that recrystallization occurs. In addition, percentage pass reduction is large, and the deformation heat effect is also larger, partly compensates the heat loss in the operation of rolling, improves the temperature in the steel plate deformation process, promotes the recrystallization of deformed microstructure. Control roughing finishing temperature 〉=980 ℃, best 〉=1000 ℃, purpose is to promote the rough rolling plate blank recrystallization. In finishing stands, in the several frames in tandem rolling unit front, have at least a frame to adopt the comparatively coarse roll of roll surface, the roll surface roughness is μ m at least 〉=5, best 〉=7 μ m, purpose is the frictional force that increases between steel plate and the roll, strengthen the shearing deformation of steel plate, increase shearing deformation along the penetration depth of thickness of slab direction, reduce the plane strain district in steel plate centre, the deformation that increases the steel plate center stores energy, promotes the recrystallization of hot rolled plate, destroys thick (100) columanar structure of original as cast condition.
At last, hot rolled plate is through 〉=710 ℃ of high temperature coilings, realize hot rolled plate self annealing process, because 710 ℃ of critical-temperatures that are higher than recrystallization, Static Recrystallization occurs at 710 ℃ in hot rolled plate more than the temperature, eliminate (100)＜011〉deformed microstructure, the isometry of realization hot rolled plate tissue, and promote hot rolled plate crystal grain, ALN, MnS particle to grow up, improve finished product magnetic. Through above-mentioned process optimization, not only eliminate the corrugated defective fully, and can save normalizing, and obtain the non-oriented magnetic steel sheet of Apparently in Good Order﹠ Condition, electromagnetic performance excellence.
Also can hot rolled strip be carried out normalizing at 950～1050 ℃ process according to concrete product performance demands situation, make hot-strip organize further thickization of homogenising, obtaining more preferably, texture distributes and the more excellent non-oriented electromagnetic steel sheet of electromagnetic performance.
Because the Al content of high grade non-oriented electrical steel and Si content are high, the anisotropy of electromagnetic performance strengthens, and this also has influence on heating and the efficient of motor. For the anisotropy that the rising that reduces owing to Si and Al causes, the present invention has adopted the method that increases cold rolling reduction ratio, by inferior method, is not only anisotropy and improves, and also is conducive to promote simultaneously the development of (100) favorable texture. For anisotropy Sensitivity Index Kp=(P15/50C-P15/50L)/(P15/50C+P15/50L) meet consumers' demand (wherein C and L represent respectively band steel vertical, horizontal) that guarantees product, cold rolling reduction ratio is controlled at 84%～92%.
In order to obtain desirable final finished tissue and texture, can obtain by programming rate, cooling velocity and the soaking temperature etc. of controlling final recrystallization annealing process, programming rate is controlled at 〉=25 ℃/s, slow cooling speed is controlled at≤15 ℃/s (1100 ℃ → 600 ℃), and fast speed of cooling is controlled at～30 ℃/s. Because alloy system of the present invention is favourable to adjusting the band structure of steel so that can be controlled at higher level with the steel annealing temperature; Soaking temperature is controlled at 900 ℃～1100 ℃, if γ → α phase transformation can partly occur too high (＞1100 ℃) steel band, destroys recrystallization and recrystallized structure. By control slow cooling speed, also can reduce to be with the steel thermal stress, thereby obtain better electromagnetic performance. Annealing atmosphere adopts 30%H2+ 70%N2 to obtain smooth belt steel surface, also can prevent the formation with the steel internal oxidation layer simultaneously. The crystal grain of final products directly is 50～200 μ m.
Its production process is: molten iron preliminary treatment, smelting, double refining, continuous casting, hot rolling, (normalizing), pickling, cold rolling, finished products and dielectric film coating. The technique that wherein normalizing operation adopts when being the product of production higher level, manufacturer can select as the case may be.
Beneficial effect of the present invention
Compared with prior art, the technology of the present invention characteristics are only to carry out suitable alloy system design, need not to transform any production equipment, need not existing production technology is made Important Adjustment, just can produce iron loss and meet or exceed H8 level and the magnetic strength above high grade non-oriented electrical steel of 400 Gausses that raises, can satisfy the instructions for use of high efficiency motor iron core. Especially this product can need not normalizing, once cold rolling, need not cold rolling intermediate annealing and just can produce, and has reduced production cost, has improved product cost performance and the market competitiveness.
So the present invention in conjunction with reasonably procedure technology control, reaches the purpose that the simplest production process of employing just can be produced the high grade non-oriented electrical steel with high magnetic strength on the basis of optimizing composition.
The composition contrast situation of the present invention and Patents is as shown in table 1, and manufacture method contrast situation is as shown in table 2:
Table 1 the present invention and related invention composition contrast information slip (%)
| C | Si | Al | Mn | P | S | Sn | Sb | B | N | |
| The present invention | 0.005 | 1.5～2.5 | 0.8～1 .3 | 0.2～0 .5 | 0.03 | 0.005 | 0.05～ 0.12 | 0.03～0 .1 | 0.0005～ 0.004 | 0.003 |
| 95119969.2 | ＜0.01 | ＜4.0 | ＜1.5 | ＜1.5 | ＜0.2 | ＜0.01 | / | / | / | / |
| 91107594.1 | ＜0.02 | (Si+Al) | ＜4.0 | ＜1.0 | ＜0.2 | / | / | / | / | / |
| JP11172333A | / | 0.1～4.0 | / | 0.1～2 | / | / | / | / | / | / |
| .0 | ||||||||||
| 95194275.1 | / | 0.1～2.5 | 0.1～1 .0 | 0.1～2 .0 | / | / | / | / | / | / |
| Si, Al in the above element, Mn select at least a, and (Si+2Al)＜2.5%. | ||||||||||
| Patent 00133842.0 | ＜0.005 | 1.5～8.0 | / | 0.005 ～2.5 | / | ＜0.005 | / | / | / | ＜0.005 |
| The flat 11-172333 of Te Open | / | 0.1～4.0 | / | 0.1～2 .0 | / | / | / | / | / | / |
| 00115993.3 | ＜0.008 | 0.2～2.5 | ＜1.5 | 0.15～ 0.8 | -- | ＜0.003 | P+Sn/Sb：0.0 8～0.45 | ＜0.035 | ＜0.003 | |
| 01138224.4 | ＜0.005 | ＜2.0 | ＜0.00 8 | 0.15～ 0.8 | -- | ＜0.003 | P+Sn/Sb：0.0 8～0.45 | ＜0.0005 | ＜0.002 | |
| Examined patent publication 49-39526 | ＜0.04 | 1.5～4. 0 | ＜1.0 | / | / | / | / | / | / | / |
| Examined patent publication 62-54023 | ＜0.01 | 1.8％＜(Si+2A 1)＜5％ | / | / | ＜0.001 5 | / | / | / | ＜0.002 | |
Table 2 the present invention and related invention manufacture method contrast information slip
| Manufacture method | |
| The present invention | Add and separate out element, reach and improve finished product texture purpose, to improve electromagnetic performance; Suitably add B, reach the purpose that improves production stability; The employing part for Si, reaches the purpose of improving processing characteristics with Al; Course of hot rolling adopts roughing to depress greatly method, reaches elimination ' corrugated ' defective purpose. The normalizing annealing of hot-strip can be used as the means of further raising electromagnetic performance as possibility. |
| 95119969.2 | Intermediate billet temperature retaining+secondary cold-rolling. |
| 91107594.1 | Secondary cold-rolling method+intermediate annealing. |
| JP11172333A | Controlled rolling rhythm and coiling temperature. |
| 95194275.1 | Two-phase section finish to gauge+high temperature coiling and insulation. |
| 00133842.0 | Normalizing annealing+secondary cold-rolling. |
| The flat 11-172333 of Te Open | High Mn+ high temperature coiling and insulation. |
| 00115993.3 | High Si+Al also adjusts the composition system of P+Sn/Sb. |
| 01138224.4 | Do not contain the composition system of Al and adjust P+Sn/Sb. |
| Examined patent publication 49-39526 | The low temperature casting method. |
| Examined patent publication 62-54023 | The cooling of not spraying water in 1～7 second after finish to gauge and the hot rolling more than 1000 ℃, and batch at＜700 ℃. |
Description of drawings
Fig. 1 is that steel C hot rolled plate of the present invention is organized schematic diagram;
Fig. 2 organizes schematic diagram after the steel C Hot Rolled Plate Normalizing annealing of the present invention;
Fig. 3 is that steel C production board of the present invention is organized schematic diagram;
Fig. 4 is Related product of the present invention and conventional 35A230 electromagnetic performance contrast schematic diagram.
The specific embodiment
Embodiment 1:
Invention steel A contains C:0.0031%, Si:2.00%, Al:0.95%, Mn:0.31%, Sn:0.092%, B:0.0009%, and all the other are iron and inevitable impurity; Roughing accumulative total reduction ratio 84%, the reduction ratio 41% of one of them passage, 1000 ℃ of roughing finishing temperatures; The finish rolling start rolling temperature is 918 ℃, and finishing temperature is 868 ℃, and 560 ℃ are batched, and the finish rolling reduction ratio is respectively: the first passage 31%, the second passage 29%, the 3rd passage 29%, four-pass 71%, the 5th passage 18 %; Do not adopt normalizing annealing; Cold rolling reduction ratio is 87% (finished strip thickness is 0.35mm); The recrystallization annealing system: 1000 ℃ * 90 seconds, heating rate was 30 ℃/s, and slow cooling speed is controlled at≤15 ℃/s (1000 ℃ → 600 ℃), and fast speed of cooling is controlled to be 33 ℃/s. Annealing atmosphere adopts 30%H2+70%N2. The production board surface quality is good, and average crystal grain directly is 120 μ m, and magnetic is: B50=1.718T, P15/50=2.132W/kg. Product was by 250 ℃ * 100 hours, and electromagnetic performance is deteriorated without timeliness.
Embodiment 2:
Invention steel B contains C:0.0029%, Si:2.00%, Al:0.99%, Mn:0.301%, Sb:0.078%, B:0.0009%, and all the other are iron and inevitable impurity; Roughing accumulative total reduction ratio 85%, the reduction ratio 42% of one of them passage, 990 ℃ of roughing finishing temperatures; The finish rolling start rolling temperature is 916 ℃, and finishing temperature is 868 ℃, and 729 ℃ are batched, and the finish rolling reduction ratio is respectively: the first passage 31%, the second passage 29%, the 3rd passage 30%, four-pass 71%, the 5th passage 17 %; Do not adopt normalizing; Cold rolling reduction ratio is 87.5% (finished strip thickness is 0.35mm); The recrystallization annealing system: 1000 ℃ * 70 seconds, heating rate was 28 ℃/s, and slow cooling speed is controlled at≤15 ℃/s (1000 ℃ → 600 ℃), and fast speed of cooling is controlled to be 31 ℃/s. Annealing atmosphere adopts 30%H2+70% N2. The production board surface quality is good, and average crystal grain directly is 125 μ m, and magnetic is: B50=1.726T, P15/50=2.125W/kg. Product was by 250 ℃ * 100 hours, and electromagnetic performance is deteriorated without timeliness.
Embodiment 3:
Invention steel C contains C:0.0030%, Si:2.01%, Al:1.02%, Mn:0.302%, Sn:0.1%, B:0.001%, and all the other are iron and inevitable impurity; Roughing accumulative total reduction ratio 83%, the reduction ratio 42% of one of them passage, 1000 ℃ of roughing finishing temperatures; The finish rolling start rolling temperature is 915 ℃, and finishing temperature is 872 ℃, and 725 ℃ are batched, and the finish rolling reduction ratio is respectively: the first passage 30%, the second passage 30%, the 3rd passage 30%, four-pass 70%, the 5th passage 17%; Normalizing system: 1000 ℃ * 120 seconds; Cold rolling reduction ratio is 86.5% (finished strip thickness is 0.35mm); The recrystallization annealing system: 1000 ℃ * 80 seconds, heating rate was 28 ℃/s, and slow cooling speed is controlled at≤15 ℃/s (1000 ℃ → 600 ℃), and fast speed of cooling is controlled to be 30 ℃/s. Annealing atmosphere adopts 30%H2+70%N2. The production board surface quality is good, and average crystal grain directly is 135 μ m, and magnetic is: B50=1.732T, P15/50=2.112W/kg. Product was by 250 ℃ * 100 hours, and electromagnetic performance is deteriorated without timeliness.
The chemical composition of specific embodiment and manufacture method and electromagnetic performance are shown in table 3, table 4, and we can find out that composition of the present invention and manufacturing process go for the high grade non-oriented electrical steel product of H7～H12 series.
Table 3 wt%
| Embodiment | C | Si | Al Sol | Mn | P | S | Sn | Sb | B | N |
| 1 | 0.0031 | 2.00 | 0.95 | 0.31 | 0.020 | 0.0035 | 0.092 | 0 | 0.0009 | 0.0025 |
| 2 | 0.0029 | 2.00 | 0.99 | 0.301 | 0.025 | 0.0040 | 0 | 0.078 | 0.0009 | 0.0029 |
| 3 | 0.0030 | 2.01 | 1.02 | 0.302 | 0.028 | 0.0040 | 0.100 | 0 | 0.0010 | 0.0020 |
| 4 | 0.0035 | 1.50 | 0.80 | 0.25 | 0.021 | 0.0045 | 0.080 | 0 | 0.0008 | 0.0020 |
| 5 | 0.0025 | 1.50 | 1.30 | 0.29 | 0.015 | 0.0030 | 0 | 0.090 | 0.0030 | 0.0028 |
| 6 | 0.0030 | 1.80 | 1.00 | 0.35 | 0.016 | 0.0030 | 0 | 0.060 | 0.0005 | 0.0021 |
| 7 | 0.0025 | 2.20 | 0.80 | 0.50 | 0.015 | 0.0025 | 0 | 0.075 | 0.0005 | 0.0015 |
| 8 | 0.0040 | 2.20 | 1.30 | 0.50 | 0.018 | 0.0025 | 0.110 | 0 | 0.0010 | 0.0012 |
| 9 | 0.0035 | 2.50 | 0.90 | 0.45 | 0.016 | 0.0020 | 0.060 | 0.050 | 0.0010 | 0.0018 |
| 10 | 0.0025 | 2.50 | 0.80 | 0.45 | 0.010 | 0.0020 | 0.050 | 0.040 | 0.0008 | 0.0029 |
| 11 | 0.0020 | 2.30 | 1.30 | 0.20 | 0.028 | 0.0035 | 0.080 | 0 | 0.0040 | 0.0025 |
| 12 | 0.0015 | 2.30 | 1.00 | 0.35 | 0.025 | 0.0025 | 0 | 0.095 | 0.0030 | 0.0028 |
Table 4: embodiment production method and finished product electromagnetic performance
| Manufacturing process | Slab heating temperature (℃) | Roughing maximum depression rate (%)/total reduction (%) | Maximum planishing roll surface roughness (μ m) | The roughing finishing temperature (℃) | Coiling temperature (℃) | The normalizing annealing temperature (℃) | Cold rolling total reduction (%) | The finished products temperature (℃) | Electromagnetic performance | Affiliated series | |
| P 15/50 (W Kg) | B 50 (T) | ||||||||||
| 1 | 1150 | 41/84 | 8 | 1000 | 560 | Nothing | 87.0 | 1000 | 2.132 | 1.718 | H8 |
| 2 | 1120 | 42/85 | 7 | 990 | 729 | Nothing | 87.5 | 1000 | 2.125 | 1.726 | H8 |
| 3 | 1130 | 42/83 | 9 | 1000 | 725 | 1000 | 86.5 | 1000 | 2.112 | 1.732 | H8 |
| 4 | 1180 | 41/82 | 6 | 1050 | 720 | Nothing | 89.1 | 920 | 2.650 | 1.740 | H12 |
| 5 | 1135 | 41/83 | 7 | 1000 | 710 | Nothing | 86.6 | 950 | 2.350 | 1.738 | H10 |
| 6 | 1110 | 43/82 | 6 | 1000 | 730 | Nothing | 85.2 | 960 | 2.250 | 1.730 | H9 |
| 7 | 1100 | 43/83 | 8 | 1050 | 735 | Nothing | 86.5 | 1000 | 2.125 | 1.734 | H8 |
| 8 | 1130 | 41/81 | 12 | 1000 | 745 | Nothing | 84.6 | 1000 | 1.960 | 1.712 | H7 |
| 9 | 1155 | 42/82 | 6 | 985 | 570 | 1000 | 88.1 | 1050 | 1.910 | 1.725 | H7 |
| 10 | 1145 | 43/81 | 11 | 995 | 740 | Nothing | 87.5 | 1000 | 1.950 | 1.712 | H7 |
| 11 | 1160 | 42/83 | 7 | 1000 | 725 | 1050 | 85.5 | 1050 | 1.920 | 1.718 | H7 |
| 12 | 1100 | 42/82 | 10 | 980 | 730 | Nothing | 86.3 | 1000 | 1.980 | 1.715 | H7 |
Fig. 1 is hot rolled plate metallographic structure figure among the C of the present invention (example 3), hot rolling microstructure is desirable ferrite, do not have ' banded structure ' of segregation to occur with the steel middle part, nearly belt steel surface fine microstructures is even, and centre crystal grain is along rolling direction extension, thicker.
Fig. 2 is that hot-strip is through the metallographic structure figure after the normalizing annealing among the C of the present invention (example 3), and obviously than even after the hot rolling, thick, the crystal grain behind the hot rolling deformation has been finished recrystallization process to the hot-rolled strip structure of steel after the normalizing annealing.
Figure 3 shows that the metallographic structure figure of C of the present invention (example 3) final finished, grain structure is more satisfactory, and average crystal grain directly reaches about 140 μ m, can be hanged down iron loss and higher magnetic induction intensity.
Electromagnetic performance more as shown in Figure 4 for the product that adopts technique of the present invention and common process (the same trade mark series of products of 35A230 contrast), adopt alloy system of the present invention, add Sn/Sb, rolling, control hot rolling is depressed greatly in roughing and the methods such as cold rolling reduction ratio, can obtain excellent surface quality, the have high magnetic strength high grade non-oriented electrical steel of (exceeding more than the 0.05T (500 Gauss) than conventional products), when guaranteeing that iron loss (P15/50) to a certain degree reduces, magnetic strength obtains the raising of quite large degree, when being used for making motor, be conducive to improve the efficient of motor, reach the purpose of energy savings. If the employing normalizing process then can obtain the product of electromagnetic performance more superior (iron loss is lower), thereby further improve the class of product.
According to the present invention, can prevent that timeliness is deteriorated by C, N content in the control steel, adopt new alloy system, roughing to depress greatly, adjust the distribution of finish rolling reduction ratio, high temperature coiling technique, adopt large cold rolling reduction ratio and control final recrystallization annealing system, not only can obtain the high grade non-oriented electrical steel plate (product quality in kind meets or exceeds the H8 of Nippon Steel level) of the high magnetic strength of having of excellent surface quality, low iron loss, and can reduce the anisotropy of product, can improve better the efficient of motor. And the present invention can adopt normalizing process targetedly according to the user of some high-end demands, further obtains the more superior product of electromagnetic performance.
In sum; because the technology of the present invention adopt to be added segregation element, the large Reduction Technology of roughing, does not use electromagnetic agitation (EMS), is not used normalizing annealing, (non-oriented electrical steel of H7～H14), product is magnetic strength (B under the prerequisite that keeps low iron loss with regard to the producible high trade mark with high magnetic strength for the once cold rolling method50) will improve more than 500 Gausses than the magnetic strength of conventional products; And; can omit Hot Rolled Plate Normalizing technique, also can adopt once cold rolling technique according to the production actual conditions; need not any scrap build; thereby be the method for the good high grade non-oriented electrical steel of a kind of technique production performance simple, with low cost, have very strong adaptability, economy and the feature of environmental protection.
Claims (7)
1. the high grade non-oriented electrical steel that has high magnetic strength, its composition percentage by weight is:
C：≤0.0050％
N：≤0.0030％
Si：1.50％～2.50％
Al：0.80％～1.30％
Mn：0.20％～0.50％
P：≤0.030％
S：≤0.005％
Sb：0.03％～0.10％
Sn：0.05％～0.12％
B：0.0005％～0.0040％
All the other are iron and inevitably are mingled with;
Wherein, Sb and Sn select wherein a kind of.
2. the high grade non-oriented electrical steel with high magnetic strength as claimed in claim 1 is characterized in that the percentage by weight of its composition is:
C：≤0.0030％
N：≤0.0015％
Si：1.80％～2.20％
Al：0.80％～1.20％
Mn：0.30％～0.50％
P：≤0.030％
S：≤0.003％
Sb：0.05％～0.10％
Sn：0.06％～0.11％
B：0.0005％～0.0030％
All the other are iron and inevitably are mingled with;
Wherein, Sb and Sn select wherein a kind of.
3. the manufacture method that has the high grade non-oriented electrical steel of high magnetic strength
A. hot rolling: heating of plate blank: 1100～1200 ℃ of slab heating temperatures;
Roughing: roughing≤4 passages, accumulative total reduction ratio 〉=80% wherein has the reduction ratio of a passage 〉=40% at least, roughing finishing temperature 〉=980 ℃;
Finish rolling: in the several frames in tandem rolling unit front, have at least a frame to adopt the comparatively coarse roll of roll surface, the roll surface roughness is μ m at least 〉=5;
Batch: 〉=710 ℃ of high temperature coilings, realize hot rolled plate self annealing process;
B. cold rolling: cold rolling reduction ratio is controlled at 84%～92%;
C. recrystallization annealing: soaking temperature is controlled at 900 ℃～1100 ℃.
4. the manufacture method with high grade non-oriented electrical steel of high magnetic strength as claimed in claim 3 is characterized in that, the hot rolled plate after batching carries out normalizing annealing, 950～1050 ℃ of normalizing annealing temperature.
5. the manufacture method with high grade non-oriented electrical steel of high magnetic strength as claimed in claim 3 is characterized in that, the reduction ratio of 2 above passages of roughing 〉=40%.
6. the manufacture method with high grade non-oriented electrical steel of high magnetic strength as claimed in claim 3 is characterized in that, control roughing finishing temperature 〉=1000 ℃.
7. the manufacture method with high grade non-oriented electrical steel of high magnetic strength as claimed in claim 3 is characterized in that, control planishing roll surface roughness 〉=7 μ m.
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