CN103849810A - Non-oriented silicon steel and manufacture method thereof - Google Patents
Non-oriented silicon steel and manufacture method thereof Download PDFInfo
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Abstract
The invention provides a non-oriented silicon steel with excellent magnetism and a manufacture method thereof. In the manufacture method, the relationship among the temperature T, the carbon content [C], and the free oxygen content [O] of the molten steel in the converter tapping process of steel-making can be represented by a formula: 7.27*103<=[O][C]e(-5000/T)<=2.99*104; and a low-temperature tension short-time annealing technology is adopted in the final annealing step. The manufacture method provided by the invention can produce non-oriented silicon steel having low iron loss and excellent iron-loss anisotropy.
Description
Technical Field
The present invention relates to non-oriented silicon steel and a method for manufacturing the same, and more particularly, to non-oriented silicon steel having excellent iron loss and iron loss anisotropy, and a method for manufacturing the same.
Background
The non-oriented silicon steel is mainly used for manufacturing stator cores of medium and large motors (> 50 HP) and generators and stator and rotor cores of small motors with high energy efficiency requirements. To achieve miniaturization and energy saving of electronic devices, it is required that the used non-oriented silicon steel have low iron loss and excellent anisotropy of iron loss.
The conventional method for manufacturing non-oriented silicon steel is to increase the resistance of silicon steel by using a billet containing silicon of 2.5wt% or more and aluminum of 0.2wt% or more, thereby reducing the iron loss of the non-oriented silicon steel. However, this method requires a final annealing temperature of 1000 ℃ or higher, and therefore has problems of high cost, furnace rod clogging, and the like.
In order to obtain non-oriented silicon steel meeting the requirements of miniaturization and energy conservation of electronic equipment, people have developed the non-oriented silicon steel
Many studies have been made on the manufacturing process, and the development of non-oriented silicon steel having excellent magnetic properties has been attempted.
US patent US4560423 uses a cast slab comprising, in weight percent:
si is more than or equal to 2.5 percent, Al is more than or equal to 1.0 percent, 3.5 percent to (Si + Al) is less than or equal to 5.0 percent, S is less than or equal to 0.005 percent, and N is less than or equal to 0.004 percent, and two-stage annealing is adopted, namely heat preservation is carried out at 850-1000 ℃ for 30-120 seconds, then heat preservation is carried out at 1050 ℃ for 3-60 seconds, and iron loss P is obtained15/50Non-oriented silicon steel with the thickness less than or equal to 2.70W/kg (silicon steel with the thickness of 0.5 mm).
Japanese laid-open patent JP1996295936S uses a cast slab comprising the following components in weight percent: c <0.005%, Si: 2.0-4.0%, Al: 0.05-2%, Mn: 0.05-1.5%, P is less than or equal to 0.1%, S is less than or equal to 0.003%, N is less than 0.004%, Sn: 0.003-0.2%, Cu: 0.015 to 0.2%, 0.01 to 0.2% of Ni, Cr: 0.02-0.2%, V: 0.0005-0.008% and Nb <0.01%, and the non-oriented silicon steel with low iron loss is obtained by controlling the normalizing cooling speed to be below 80 ℃/S, controlling the cold rolling reduction to be above 88% and finally carrying out two-stage annealing.
US6139650 controls S content, surface nitrogen content and the like in silicon steel by adding Sb, Sn, rare earth elements Se, Te and the like into a cast slab to control iron loss P of the silicon steel15/50The thickness of the silicon steel (0.5 mm) is controlled to be less than 2.40W/kg.
Although the iron loss of the silicon steel is controlled to a low level in the prior art, the iron loss anisotropy is not involved in the prior art, and it is known that the iron loss anisotropy of the silicon steel directly affects the rotation loss of the stator and rotor cores and is one of the key factors for obtaining excellent loss characteristics of electric equipment. Therefore, the research and development of the non-oriented silicon steel with low iron loss and excellent iron loss anisotropy have important significance and wide application prospect.
Disclosure of Invention
The invention aims to provide non-oriented silicon steel with excellent magnetism and a manufacturing method thereof. The non-oriented silicon steel has low iron loss (the iron loss P of the silicon steel at the thickness of 0.5 mm)15/502.40W/kg or less) and excellent iron loss anisotropy (10 percent or less), can meet the use requirements of iron core materials of medium and large generators, motors and small and high-efficiency motors. In addition, the method has the advantages of low cost, stable effect and the like.
The invention relates to a method for manufacturing non-oriented silicon steel, which sequentially comprises the following steps: a) steel making, b) hot rolling, c) normalizing, d) cold rolling, and e) annealing, characterized in that,
obtaining a cast slab comprising the following components in weight percent by the steelmaking step a): 0.001-0.004% of C, 2.5-4.0% of Si, 0.5-1.5% of Al, 0.10-1.50% of Mn, less than or equal to 0.02% of P, less than or equal to 0.002% of S, less than or equal to 0.003% of N, less than or equal to 0.005% of B, more than or equal to 300% of Mn/S, more than or equal to 300% of Al/N, and the balance of Fe and inevitable impurities; wherein,
the steelmaking step a) comprises converter steelmaking, wherein the molten steel temperature T (unit is K) and the carbon content [ C ] of converter tapping](in ppm) and free oxygen content [ O ]](in ppm) satisfies the following formula: 7.27X 103≤[O][C]e（-5000/T）≤2.99×104(ii) a And
in the annealing step e), the cold-rolled steel strip after cold rolling is heated to 900-1050 ℃, and heat preservation is carried out under the tension sigma of 0.5-1.5MPa, wherein the heat preservation time t is 8-60 seconds.
In the method of the present invention, a cast slab is first obtained by steel making, then the cast slab is hot-rolled to form a hot-rolled steel strip, then the hot-rolled steel strip is normalized, then the normalized hot-rolled steel strip is cold-rolled to form a cold-rolled steel strip, and finally the cold-rolled steel strip is subjected to final annealing treatment.
In the method of the present invention, the holding time t in the annealing step e) should be limited to 8 to 60 seconds in view of reducing the manufacturing cost and contributing to the quality stability of the silicon steel product. When the holding time t is less than 8 seconds, the crystal grains are not fully coarsened, which is not beneficial to reducing the iron loss and the iron loss anisotropy of the non-oriented silicon steel. When the holding time t exceeds 60 seconds, the cost is increased, and the iron loss anisotropy of the non-oriented silicon steel are not further improved.
In the method of the present invention, it is preferable that among unavoidable impurities in the cast slab, Nb is 0.002wt% or less, V is 0.003wt% or less, Ti is 0.003wt% or less, and Zr is 0.003wt% or less.
In the method, the temperature in the annealing step e) is preferably 900-1050 ℃, and more preferably 920-1000 ℃ in terms of facilitating the growth of crystal grains and reducing the performance difference of the crystal grains in the rolling direction and the transverse direction; and the tension sigma is preferably 0.5 to 1.5MPa, more preferably 1 to 1.3 MPa. The temperature in the annealing step e) is too low to be beneficial to the growth of crystal grains; while too high a temperature in the annealing step e) is not favorable for reducing the cost and simplifying the process. Too small a tension sigma in the annealing step e) is not beneficial to rapid growth of crystal grains under low-temperature short-time annealing; when the tension sigma in the annealing step e) is too large, the performance difference of the crystal grains in the rolling direction and the transverse direction is large, which is not beneficial to reducing the iron loss anisotropy of the non-oriented silicon steel.
In the method of the present invention, it is preferable that the ingot in the steelmaking step a) further contains Sn and/or Sb, wherein the Sb +2Sn content is 0.001 to 0.05wt%, in view of further reducing the N, O content in the surface layer of the final silicon steel product and improving the crystal texture of the silicon steel product.
In the method of the present invention, the steel-making step a) further includes RH refining, and in order to improve the deoxidation effect, it is preferable that in the RH refining, deoxidation is performed using a FeSi alloy at the end of decarburization, and then deoxidation is performed using a FeAl alloy.
In the method of the present invention, the normalizing step c) may be performed by a hood-type furnace normalizing or a continuous annealing. In view of further reducing the iron loss anisotropy, obtaining a good sheet shape, and facilitating the cold rolling, it is preferable that the hood-type furnace normalization is performed under the following conditions: preserving the heat for 2-6 hours at 780-880 ℃ under the protection of nitrogen and hydrogen; or preferably, the normalization in the continuous annealing mode is performed under the following conditions: heating the hot rolled steel strip to 850-950 ℃ at a heating speed of 5-15 ℃/s, preserving heat under the protection of nitrogen for 10-90 seconds, cooling to 650 ℃ at a cooling speed of less than 10 ℃/s, and naturally cooling.
In the method of the present invention, it is preferable that the reduction ratio in the cold rolling step d) is 70 to 88% in view of further reducing the iron loss anisotropy.
In the method of the present invention, it is preferable that the amount of deformation of 950 ℃ or more in the hot rolling step b) is 80% or more in view of further improving the grain structure of the final silicon steel product. Further, the maximum temperature difference between different portions of the hot rolled steel strip is preferably 20 ℃ or less, more preferably 10 ℃ or less, in view of obtaining a good plate shape and preventing edge cracking.
The present invention provides a non-oriented silicon steel having low iron loss and excellent iron loss anisotropy, which can be manufactured by the above-described manufacturing method of the present invention using a cast slab containing 2.5 to 4.0wt% of Si, and which has a grain diameter of 100 to 200 μm and an equiaxial coefficient L of 1.05 to 1.35.
Further, preferably, the casting blank further comprises the following components in percentage by weight: 0.001-0.004% of C, 0.5-1.5% of Al, 0.10-1.50% of Mn0.02% of P or less, 0.002% or less of S, 0.003% or less of N, 0.005% or less of B, more than or equal to Mn/S300, more than or equal to Al/N300, and the balance of iron and inevitable impurities.
Further, it is preferable that the total content of nitrogen and oxygen at a position 30 μm below the surface of the non-oriented silicon steel of the present invention is 300ppm or less.
Further, it is preferable that the number of inclusions having a size of 500nm or less in the non-oriented silicon steel of the present invention is 40% or less.
In the invention, the quantity of inclusions can be reduced and the form can be controlled by strictly controlling the relation between the molten steel temperature T of converter tapping and [ C ] and [ O ] and controlling the content of each component in the casting blank, thereby improving the structure of the non-oriented silicon steel and improving the magnetism of the non-oriented silicon steel.
Further, in the annealing step e), by applying an appropriate tension and annealing at an appropriate temperature for a short time, the crystal grains can be rapidly grown and the difference in the properties of the crystal grains in the rolling direction and the transverse direction is small, thereby contributing not only to the reduction of the iron loss but also to the reduction of the anisotropy of the iron loss.
The invention controls the content of each component in the casting blank through steelmaking and strictly controls the molten steel temperature T and [ C ] of converter tapping]And [ O]The amount of inclusions is reduced and the morphology is controlled, and low-temperature tension short-time annealing is performed to control the crystal grain morphology, so that non-oriented silicon steel with excellent iron loss and iron loss anisotropy can be obtained. The non-oriented silicon steel of the invention has iron loss P15/502.40W/kg or less (0.5 mm thick silicon steel), and an iron loss anisotropy of 10% or less, wherein P15/50The iron loss is 50Hz and 1.5T magnetic induction intensity.
Drawings
FIG. 1 shows Mn/S ratio in a cast slab for manufacturing non-oriented silicon steel and core loss P of the non-oriented silicon steel15/50The relationship (2) of (c).
FIG. 2 shows the sulfur content in the cast slab used for manufacturing non-oriented silicon steel and the iron loss P of the non-oriented silicon steel15/50The relationship (2) of (c).
FIG. 3 shows the ratio of Al/N in the cast slab used to make non-oriented silicon steel to that of non-oriented silicon steelIron loss P15/50The relationship (2) of (c).
FIG. 4 shows the total nitrogen and oxygen content at 30 μm below the surface of the non-oriented silicon steel and the iron loss P of the non-oriented silicon steel15/50The relationship (2) of (c).
FIG. 5 is a graph showing the relationship between the equiaxed grain size of non-oriented silicon steel and the iron loss anisotropy of non-oriented silicon steel.
Detailed Description
First, the reasons for limiting the components in the cast slab for producing non-oriented silicon steel according to the present invention will be described below.
Si: can be dissolved in ferrite to form a substitutional solid solution, improves the resistivity of a matrix, can obviously reduce the iron loss and improve the yield strength, and is one of the most important alloy elements in the non-oriented silicon steel. When the content of Si is too low, the advantageous effect of reducing the iron loss is not significant, and when the content of Si is too high, not only the effect of reducing the iron loss is significantly reduced, but also the processing is difficult. In the present invention, the silicon content is defined as 2.5 to 4.0 wt%.
Al: can be dissolved in ferrite to improve the resistivity of a matrix, coarsens crystal grains, reduces iron loss and improves yield strength, and can also deoxidize and fix nitrogen, but is easy to cause internal oxidation of the surface layer of a finished steel plate. When the Al content is too low, the beneficial effects of reducing iron loss, deoxidizing and fixing nitrogen are not obvious, and when the Al content is too high, smelting and pouring are difficult, magnetic induction is reduced, and processing is difficult. In the present invention, the aluminum content is limited to 0.5 to 1.5 wt%.
Mn: the resistivity of the steel can be increased and the iron loss can be reduced like Si and Al, stable MnS can be formed with an impurity element S, the harm of S to magnetism can be eliminated, in addition, the existence of Mn can also prevent hot brittleness, the Mn can also be dissolved in ferrite to form a substitutional solid solution, the solid solution strengthening effect can be realized, and the yield strength of a matrix can be improved. When the Mn content is too low, the above advantageous effects are not significant, and when the Mn content is too high, the transformation point temperature Ac1 of the silicon steel is lowered, the recrystallization temperature is lowered, and α - γ phase transformation occurs during heat treatment, which deteriorates and contributes to the crystal texture. In the present invention, the Mn content is defined to be 0.10wt% to 1.50 wt%.
Further, the present inventors examined the Mn/S ratio and the iron loss P of non-oriented silicon steel15/50The relationship (2) of (c). FIG. 1 shows Mn/S ratio in a cast slab for manufacturing non-oriented silicon steel and core loss P of the non-oriented silicon steel15/50The relationship (2) of (c). As shown in FIG. 1, the Mn/S ratio of 300 or more is preferable for reducing the iron loss P15/50After the Mn/S ratio reaches 600, it reduces the iron loss P15/50The effect of (2) is substantially saturated. In the present invention, the Mn/S ratio is defined to be 300 or more, preferably 350 to 600.
S: is harmful to processing and magnetism, and is liable to form fine MnS particles with Mn, thereby preventing the growth of annealed grains in the finished product and seriously deteriorating the magnetism, and in addition, S is liable to form low-melting FeS and FeS with Fe2Or eutectic, causing hot work brittleness problems. The inventor researches the iron loss P of the non-oriented silicon steel according to the S content15/50The influence of (c). FIG. 2 shows the sulfur content in the cast slab used for manufacturing non-oriented silicon steel and the iron loss P of the non-oriented silicon steel15/50The relationship (2) of (c). As shown in FIG. 2, when the S content exceeds 0.002wt%, the non-oriented silicon steel has an iron loss P15/50And (4) deterioration. In the present invention, the S content is limited to 0.002wt% or less.
P: the workability of the steel strip can be improved by adding a certain amount of phosphorus to the steel, but if the content of P is too high, the cold workability of the steel strip is rather deteriorated. In the present invention, the P content is limited to 0.02% or less.
C: the excessive C increases the transformation amount of alpha and gamma phase regions during normalizing treatment, greatly reduces the transformation point temperature Ac1, causes abnormal refinement of crystal structure, and increases iron loss, and the excessive C is used as a gap element, and the content of the C is too high to be beneficial to the fatigue performance of silicon steel. The magnetic failure is caused by the C content being too high, but the yield strength is remarkably reduced by the C content being too low, and in the present invention, the C content is limited to 0.001 to 0.004 wt%.
N: the self is interstitial atom, and is easy to form fine dispersed nitride with Ti, Al, Nb and V, thus strongly hindering the growth of crystal grains and deteriorating iron loss. When the N content is too high, the amount of nitride precipitated increases, which strongly hinders the growth of crystal grains and deteriorates the iron loss. In the present invention, the N content is limited to 0.003wt% or less.
The influence of N elements and other fine N compounds is generally reduced by increasing the Al content to form coarsened AlN. The Al/N ratio directly affects the form and size of AlN, and if the Al content is low, fine needle-like AlN, which seriously affects the movement of magnetic domains, is formed, thereby deteriorating the iron loss. The inventors have investigated the Al/N ratio and the iron loss P of non-oriented silicon steel15/50The relationship (2) of (c). FIG. 3 shows the Al/N ratio in the cast slab used to manufacture non-oriented silicon steel and the core loss P of the non-oriented silicon steel15/50The relationship (2) of (c). As shown in FIG. 3, when the Al/N ratio is 300 or more, preferably 350 to 600, the iron loss is low, and when the Al/N ratio exceeds 600, the effect of reducing the iron loss tends to be saturated. In the present invention, the Al/N ratio is defined to be 300 or more, preferably 350 to 600.
O is harmful to magnetism, can form oxide inclusions in the steelmaking process, and has great influence on the magnetism in quantity and shape, so that the quantity of the oxides is reduced and the shape of the oxides is controlled through the steelmaking process besides reducing the final oxygen content in the steelmaking process as much as possible.
B: b is added into the low-Si steel to reduce the Al content and the steel-making cost; b is added into the high-Si high-Al steel and is in a solid solution state, the segregation of the solid solution B along a grain boundary can improve the crystal texture, meanwhile, the embrittlement of the segregation of P can be prevented, and an internal oxidation layer and an internal nitridation layer can be prevented from being formed, so that the growth of crystal grains is promoted. However, B is an interstitial atom, and too high a content thereof hinders the movement of magnetic domains and deteriorates magnetic characteristics, so that in the present invention, the B content is limited to 0.005wt% or less.
Next, the inventors examined the effect of the total content of nitrogen and oxygen in the surface layer of the non-oriented silicon steel and the equiaxed coefficient of the crystal grains on the iron loss and/or the anisotropy of the iron loss of the non-oriented silicon steel.
The total content of nitrogen and oxygen in the surface layer of the non-oriented silicon steel represents the degree of surface nitriding and internal oxidation and the total level of oxides, which directly affect the level of iron loss of the non-oriented silicon steel. FIG. 4 shows the total nitrogen and oxygen content at 30 μm below the surface of the non-oriented silicon steel and the iron loss P of the non-oriented silicon steel15/50The relationship (2) of (c). As shown in fig. 4, the iron loss of the non-oriented silicon steel increases as the total content of nitrogen and oxygen increases, and the non-oriented silicon steel has a lower iron loss when the total content of nitrogen and oxygen is 300ppm or less. Therefore, in order to obtain non-oriented silicon steel with low iron loss, the total content of nitrogen and oxygen in the surface layer of the non-oriented silicon steel should be reduced as much as possible.
The "crystal equiaxed coefficient" in the present invention is defined as follows: sampling in parallel with the plate surface, grinding off the surface layer to prepare a metallographic sample, observing the grain structure under a microscope, and respectively detecting the average diameter D of the grain structure in parallel with the rolling direction and in perpendicular with the rolling direction (namely, the transverse direction)L、DCThe ratio of the two is the equiaxial coefficient L of the crystal grain, i.e. L = DL/DC。
And L is used for representing the shape characteristics of the crystal grains along the rolling direction and the transverse direction. The closer the value of L is to 1, the more equiaxed the crystal grains are, and the more deviated the value of L is from 1, the more deviated the crystal grain shape is from equiaxed morphology; the larger the value of L, the longer the crystal grains are in the rolling direction and the shorter the crystal grains are in the transverse direction. FIG. 5 is a graph showing the relationship between the equiaxed grain size of non-oriented silicon steel and the iron loss anisotropy of non-oriented silicon steel. As shown in fig. 5, the non-oriented silicon steel has a low iron loss anisotropy at an L value of 1.05 to 1.35. Therefore, in order to obtain non-oriented silicon steel with better magnetic properties, the equiaxial coefficient L of the crystal grains is preferably between 1.05 and 1.35.
In a preferred embodiment of the method of the present invention, a deoxidation method in which deoxidation is performed using a FeSi alloy and then deoxidation is performed using a FeAl alloy is employed in RH refining. FeSi alloy is firstly adopted for deoxidation, so that most of free oxygen in the silicon steel can be effectively removed, and a deoxidation product SiO generated by the method2The particle size is larger, so that the floating is easierRemoving; and then, by adopting FeAl alloy with deoxidation capability superior to FeSi, the residual free oxygen in the silicon steel can be removed easily, so that the amount of oxide inclusions in the silicon steel is reduced obviously, and the amount of oxide inclusions below 500nm in the final silicon steel product is not more than 40%, thereby weakening the pinning effect of a crystal boundary and the magnetic domain pinning effect and improving the magnetism of the silicon steel. The effects of FeSi alloy deoxidation and FeAl alloy deoxidation on inclusions in silicon steel are shown in Table 1.
TABLE 1
In another preferred embodiment of the method of the present invention, in the hot rolling step b), the deformation amount of 950 ℃ or more is 80% or more. The influence of the high-temperature deformation (deformation of 950 ℃ or higher) on the steel strip structure during hot rolling is shown in Table 2. As is clear from Table 2, increasing the high-temperature deformation during hot rolling reduces fine precipitates in the steel strip and improves the recrystallization of the crystal grains. Therefore, in order to obtain non-oriented silicon steel having excellent magnetic properties, in the method of the present invention, it is preferable that the amount of deformation of 950 ℃ or more in the hot rolling step b) is 80% or more.
TABLE 2
| Deformation of 950 ℃ or higher | Fine precipitates | |
|
| 1 | 30% | Is obviously visible | Core fiber texture |
| 2 | 50% | Is obviously visible | Core fiber texture |
| 3 | 60% | It can be seen that | Core with few |
| 4 | 80% | Is rarely | Complete recrystallization |
| 5 | 85% | Is rarely | Complete recrystallization |
In another preferred embodiment of the method of the present invention, the maximum temperature difference between different portions of the hot rolled steel strip in the hot rolling step is preferably 20 ℃ or less, more preferably 10 ℃ or less. The relationship between the maximum temperature difference between the center and the edge of the steel strip and the maximum crown and edge crack is shown in Table 3. As can be seen from Table 3, the convexity and edge cracks reached good levels at a temperature difference of 20 ℃ or less, and edge cracks were substantially avoided at a temperature difference of 10 ℃ or less. Therefore, in view of obtaining a good plate shape and preventing edge cracking, the maximum temperature difference between different portions of the hot rolled steel strip is preferably 20 ℃ or less, and more preferably 10 ℃ or less.
TABLE 3
| Maximum temperature difference (. degree. C.) between center and edge | Maximum | Edge crack | ||
| 1 | 10 | 30μm | Without edge crack | |
| 2 | 15 | 30μm | With occasional edge cracks | |
| 3 | 20 | 35μm | |
|
| 4 | 30 | 50μm | With edge cracks | |
| 5 | >35 | 60μm | Obvious edge crack |
The present invention will be described in more detail with reference to the following examples, but the scope of the present invention is not limited to these examples.
Example 1
Firstly, steel making is carried out, namely, a casting blank which comprises the following components in percentage by weight is obtained through RH refining and continuous casting: 0.002% of C, 3.2% of Si, 0.7% of Al, 0.50% of Mn, 0.014% of P, 0.001% of S, 0.002% of N, 0.002% of B, 0.001% of Nb0.002% of V, 0.0015% of Ti, 0.001% of ZrC, 0.008% of SnC and the balance of Fe and inevitable impurities; wherein in the steel making process, the molten steel temperature T and the carbon content [ C ] of the converter tapping steel]And free oxygen content [ O]Satisfies the following formula: 7.27X 103≤[O][C]e(-5000/T）≤2.99×104And a deoxidation mode that FeSi alloy is firstly used and then FeAl alloy is used for deoxidation is adopted in RH refining.
And hot rolling, namely heating the casting blank to 1100 ℃, preserving heat and then rolling, wherein the final hot rolling temperature is more than 850 ℃, the deformation of more than 950 ℃ is more than 80 percent, and the thickness of the hot rolled steel strip after hot rolling is 1.5-3.0 mm.
And then normalizing the hot rolled steel strip by adopting a continuous annealing mode or normalizing the hot rolled steel strip by adopting a bell-type furnace. When the continuous annealing mode is adopted for normalizing, normalizing for 10-90 seconds at 850-950 ℃, wherein the normalizing heating speed is 5-15 ℃/S, and the cooling speed is 5-20 ℃/S; and normalizing for 2-6 hours at 780-880 ℃ under the protection of hydrogen when a bell-type furnace is adopted for normalizing.
And cold-rolling the hot-rolled steel strip subjected to the normalizing treatment to form a cold-rolled steel strip, wherein the thickness of the cold-rolled steel strip after the cold-rolling is 0.27-0.5 mm, and the reduction rate of the cold-rolling is 70-88%.
Finally, the cold rolled steel strip was annealed, heated to 900 c at a heating rate of 25-45 c/S in a continuous annealing furnace, and annealed at that temperature under protection of hydrogen and nitrogen and a tension σ of 0.5MPa for 8-60 seconds, thereby obtaining non-oriented silicon steel of example 1.
Example 2
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing temperature was changed to 920 c in the final annealing step.
Example 3
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing temperature was changed to 1020 ℃ in the final annealing step.
Example 4
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing temperature was changed to 1050 ℃ in the final annealing step.
Example 5
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the tension σ was changed to 1MPa in the final annealing step.
Example 6
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the tension σ was changed to 1.3MPa in the final annealing step.
Example 7
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the tension σ was changed to 1.5MPa in the final annealing step.
Comparative example 1
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing temperature was changed to 850 c in the final annealing step.
Comparative example 2
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing temperature was changed to 1100 c in the final annealing step.
Comparative example 3
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the tension σ was changed to 0.3MPa in the final annealing step.
Comparative example 4
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the tension σ was changed to 2MPa in the final annealing step.
Comparative example 5
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the annealing time was changed to 5 seconds in the final annealing step.
Comparative example 6
Non-oriented silicon steel was manufactured in the same manner as in example 1, except that the molten steel temperature T and the carbon content [ C ] of converter tap in steel making were changed]And free oxygen content [ O]Does not satisfy the following formula: 7.27X 103≤[O][C]e(-5000/T)≤2.99×104。
Iron loss P of non-oriented silicon steel (0.5 mm thickness gauge) of the above examples and comparative examples15/50And the iron loss anisotropy were measured, and the results are shown in table 4.
As can be seen from the above table, the non-oriented silicon steel of the examples has lower iron loss and anisotropy of iron loss compared with the comparative example, and the iron loss P of the non-oriented silicon steel is 0.5mm thick15/502.40W/kg or less, and an iron loss anisotropy of 10% or less, wherein P15/50The iron loss is 50Hz and 1.5T magnetic induction intensity.
In addition, the inventors measured the surface properties and the grain properties of the non-oriented silicon steel in the examples. The measurement result shows that the grain diameter of the non-oriented silicon steel in the embodiment is 100-200 mu m, and the equiaxial coefficient L of the grains is 1.05-1.35. In addition, the total content of nitrogen and oxygen at 30 μm below the surface of the non-oriented silicon steel in the examples was 300ppm or less, and the number of inclusions having a size of 500nm or less was 40% or less.
Experimental results prove that the total nitrogen and oxygen content and the quantity of inclusions in the surface layer of the non-oriented silicon steel can be reduced by strictly controlling the relation between the molten steel temperature T of converter tapping and [ C ] and [ O ] and controlling the content of each component in a casting blank, so that the structure of the non-oriented silicon steel is improved, and the magnetism of the non-oriented silicon steel is improved. Furthermore, the invention can rapidly grow the crystal grains and obtain proper isometric coefficient of the crystal grains by carrying out low-temperature tension short-time annealing at the temperature of 900-1050 ℃ and the tension of 0.5-1.5MPa, thereby reducing the iron loss and the anisotropy of the iron loss and improving the magnetism of the non-oriented silicon steel.
The invention has the advantages of
The invention controls the content of each component in the casting blank through steelmaking, strictly controls the relationship between the molten steel temperature T of converter tapping and [ C ] and [ O ] to reduce the quantity of inclusions and control the form of the inclusions, and carries out low-temperature tension short-time annealing to control the form of crystal grains, thereby obtaining the non-oriented silicon steel with excellent iron loss and iron loss anisotropy. The non-oriented silicon steel can meet the requirements of miniaturization and energy conservation of electronic equipment, thereby having wide application prospect.
Claims (16)
1. A method for manufacturing non-oriented silicon steel sequentially comprises the following steps: a) steel making, b) hot rolling, c) normalizing, d) cold rolling, and e) annealing, characterized in that,
obtaining a cast slab comprising the following components in weight percent by the steelmaking step a): 0.001-0.004% of C, 2.5-4.0% of Si, 0.5-1.5% of Al, 0.10-1.50% of Mn, less than or equal to 0.02% of P, less than or equal to 0.002% of S, less than or equal to 0.003% of N, less than or equal to 0.005% of B, more than or equal to 300% of Mn/S, more than or equal to 300% of Al/N, and the balance of Fe and inevitable impurities; wherein,
the steelmaking step a) comprises converter steelmaking, which comprisesTemperature T and carbon content [ C ] of molten steel tapped from medium converter]And free oxygen content [ O]Satisfies the following formula: 7.27X 103≤[O][C]e(-5000/T)≤2.99×104(ii) a And
in the annealing step e), the cold-rolled steel strip after cold rolling is heated to 900-1050 ℃, and heat preservation is carried out under the tension sigma of 0.5-1.5MPa, wherein the heat preservation time t is 8-60 seconds.
2. The method for manufacturing non-oriented silicon steel according to claim 1, wherein the temperature in the annealing step e) is 920-1000 ℃ and the tension σ is 1-1.3 MPa.
3. The method of manufacturing non-oriented silicon steel as set forth in claim 1 or 2, wherein the ingot obtained in the steelmaking step a) has a composition of 350. ltoreq. Mn/S.ltoreq.600 and 350. ltoreq. Al/N.ltoreq.600.
4. The method of manufacturing non-oriented silicon steel according to any one of claims 1 to 3, wherein the ingot further comprises Sn and/or Sb, wherein the Sb +2Sn content is 0.001-0.05 wt%.
5. The method of manufacturing non-oriented silicon steel as claimed in any one of claims 1 to 4, wherein the steelmaking step a) further comprises RH refining in which deoxidation is performed using a FeSi alloy followed by deoxidation using a FeAl alloy at the end of decarburization.
6. The method for manufacturing non-oriented silicon steel according to any one of claims 1 to 5, wherein in the cold rolling step d), the reduction rate is 70-88%.
7. The method for manufacturing the non-oriented silicon steel as set forth in any one of claims 1 to 6, wherein the normalizing step c) adopts a bell type furnace normalizing, namely, maintaining the temperature at 780-880 ℃ for 2-6 hours under the protection of nitrogen and hydrogen.
8. The method of manufacturing non-oriented silicon steel as claimed in any one of claims 1 to 6, wherein the normalizing step c) is performed by continuous annealing, in which the hot rolled steel strip after hot rolling is heated to 850 to 950 ℃ at a heating rate of 5 to 15 ℃/s, is maintained under nitrogen protection for 10 to 90 seconds, is cooled to 650 ℃ at a cooling rate of 10 ℃/s or less, and is then naturally cooled.
9. The method of manufacturing non-oriented silicon steel as claimed in claim 8, wherein the hot rolled strip after hot rolling is heated to 850-930 ℃ in the normalizing step c).
10. The method of manufacturing non-oriented silicon steel of any one of claims 1 to 9, wherein in the hot rolling step b), the amount of deformation of 950 ℃ or higher is 80% or higher.
11. The method of manufacturing non-oriented silicon steel as set forth in claim 10, wherein the maximum temperature difference between different portions of the hot rolled strip in the hot rolling step b) is 20 ℃ or less.
12. A non-oriented silicon steel is characterized in that a casting blank for manufacturing the non-oriented silicon steel contains 2.5-4.0 wt% of silicon; and
the grain diameter of the silicon steel is 100-200 mu m, and the equiaxial coefficient L of the grains is 1.05-1.35.
13. The non-oriented silicon steel of claim 12, wherein the cast slab further comprises the following components in weight percent: 0.001-0.004% of C, 0.5-1.5% of Al, 0.10-1.50% of Mn0.02% of P or less, 0.002% or less of S, 0.003% or less of N, 0.005% or less of B, more than or equal to Mn/S300, more than or equal to Al/N300, and the balance of iron and inevitable impurities.
14. The non-oriented silicon steel of claim 12 or 13, wherein the total nitrogen and oxygen content at 30 μm below the surface of the silicon steel is 300ppm or less.
15. The non-oriented silicon steel of any one of claims 12 to 14, wherein the number of inclusions in the silicon steel having a size of 500nm or less is 40% or less.
16. The non-oriented silicon steel of any one of claims 12 to 15, wherein the silicon steel has a core loss P at 0.5mm thickness15/502.40W/kg or less, and an iron loss anisotropy of 10% or less, wherein P15/50The iron loss is 50Hz and 1.5T magnetic induction intensity.
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