WO2012114383A1 - Non-oriented electromagnetic steel sheet and method for manufacturing same - Google Patents
Non-oriented electromagnetic steel sheet and method for manufacturing same Download PDFInfo
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- WO2012114383A1 WO2012114383A1 PCT/JP2011/001074 JP2011001074W WO2012114383A1 WO 2012114383 A1 WO2012114383 A1 WO 2012114383A1 JP 2011001074 W JP2011001074 W JP 2011001074W WO 2012114383 A1 WO2012114383 A1 WO 2012114383A1
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- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
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- 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
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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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- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
Definitions
- the present invention is a non-oriented electrical steel sheet, particularly a component subjected to a large stress such as a rotor of a high-speed rotating machine, such as a drive motor of a turbine generator, an electric vehicle and a hybrid vehicle, or a servo motor of a robot or a machine tool.
- the present invention relates to a non-oriented electrical steel sheet having high strength, excellent fatigue characteristics and excellent magnetic characteristics, and a method for producing the same. And this invention provides said non-oriented electrical steel sheet at lower cost than before.
- IPM embedded magnet type DC inverter control motor
- IPM embedded magnet type DC inverter control motor
- the drive motor of a hybrid vehicle with space and weight constraints is aimed at high-speed rotation of the motor and is used for the rotor of the high-speed rotation motor.
- a high-strength material is advantageous for the core material.
- rotating devices such as motors and generators use an electromagnetic phenomenon
- the iron core material is also required to have excellent magnetic properties.
- the core temperature rises due to eddy currents generated by high-frequency magnetic flux, which may cause thermal demagnetization of the embedded permanent magnet, or may cause the motor efficiency to decrease.
- a magnetic steel sheet having high strength and excellent magnetic properties as a rotor material.
- Patent Document 1 proposes a method for improving magnetic characteristics by controlling the crystal grain size to 0.01 to 5.0 mm by devising finish annealing conditions in addition to the above-described strengthening method.
- Patent Document 3 discloses that in a steel having an Si content of 2.0% or more and less than 4.0%, C is set to 0.05% or less, and among Nb, Zr, Ti, and V, Carbonitride containing 1 or 2 in the range of 0.1 ⁇ (Nb + Zr) / 8 (C + N) ⁇ 1.0, 0.4 ⁇ (Ti + V) / 4 (C + N) ⁇ 4.0 A technique that utilizes precipitation strengthening and grain refinement effects due to slag has been proposed.
- Patent Document 4 in addition to the matters described in Patent Document 3, Ni and Mn are added in a total solution of 0.3% or more and 10% or less to enhance the solid solution, and then described in Patent Document 3.
- a technique has been proposed in which Nb, Zr, Ti and V are added in the same ratio as described above to achieve both high strength and magnetic properties.
- Patent Document 5 proposes a technique for increasing the strength of steel containing 0.2 to 3.5% Si by leaving a work structure inside the steel material. Yes. Specifically, no heat treatment is performed after cold rolling, or even if it does not exceed the extent corresponding to holding at 750 ° C. for 30 seconds, preferably 700 ° C. or less, more preferably 650 ° C. or less, 600 ° C. or less , 550 ° C. or lower and 500 ° C. or lower are disclosed.
- annealing is performed at 750 ° C. ⁇ 30 seconds, and the work structure ratio is 5%, 700% ⁇ 30 seconds is 20%, and 600 ° C. ⁇ 30 seconds is 50%.
- finish annealing of non-oriented electrical steel sheets is performed using a continuous annealing furnace, and the inside of the furnace is adjusted to an atmosphere containing hydrogen gas of several percent or more in order to suppress oxidation of the steel sheet surface.
- an atmosphere containing hydrogen gas of several percent or more in order to suppress oxidation of the steel sheet surface.
- an object of the present invention is to provide a high-strength non-oriented electrical steel sheet that is excellent in magnetic properties and steel sheet quality and a method for producing the same at low cost.
- the object of the present invention is to have a tensile strength of 650 MPa or more, desirably 700 MPa or more, and good high-frequency low iron loss characteristics, for example, a W 10/400 value of a sheet thickness of 0.35 mm is 40 W / kg or less.
- the inventors conducted various studies on a high-strength electrical steel sheet that can achieve the above-described object at a high level and a method for manufacturing the same. As a result, it has been found that the addition amount and addition ratio of Ti and C are deeply involved in the balance of strength and magnetic properties of the electrical steel sheet, and by optimizing the precipitation amount of Ti carbide, high strength with excellent properties It was found that electrical steel sheets can be manufactured stably and at low cost. That is, the present invention is based on the following knowledge. (A) The presence of a relatively small amount of Ti carbide can suppress the growth of crystal grains in the final annealing of electrical steel sheets, and can be strengthened by refinement of crystal grains.
- the solid solution C not only increases the tensile strength, but also has the effect of improving the fatigue characteristics that are essentially necessary for a rotor material that rotates at high speed.
- the main alloy components usually added for the purpose of increasing the electric resistance of the electrical steel sheet and reducing the iron loss are three elements of Si, Al and Mn. There is also an effect of strengthening solid solution. Therefore, in order to achieve both high strength and low iron loss, it is effective to base on solid solution strengthening with these elements. On the other hand, excessive addition of these elements embrittles steel and makes it difficult to manufacture. Therefore, there is a limit to the addition, and the three points of solid solution strengthening, low iron loss and manufacturability are most efficiently satisfied. It is desirable to add mainly Si.
- the gist of the present invention is as follows. (I)% by mass Si: 5.0% or less, Mn: 2.0% or less, Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less, A non-oriented electrical steel sheet containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2), the balance being Fe and inevitable impurities.
- (Iv)% by mass Si: 5.0% or less, Mn: 2.0% or less, Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less,
- a steel slab containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2) is kept hot at 1000 to 1200 ° C. and then hot-rolled, and then once or in the middle Heat treatment is performed at a temperature of 800 ° C or higher and 950 ° C or lower for 30 seconds or more prior to the final annealing before the final annealing after the final thickness is obtained by cold rolling or warm rolling at least twice with annealing.
- a non-oriented electrical steel sheet that has excellent mechanical characteristics and magnetic characteristics necessary for a rotor material of a motor that rotates at high speed, and that is excellent in steel sheet quality such as a bevel and a plate shape. Further, as compared with the production of a normal non-oriented electrical steel sheet, it is possible to stably produce with a high yield without adding much cost, severe manufacturing restrictions, and new processes. Therefore, it can be adapted to fields that require higher speed rotation in the future, such as drive motors for electric vehicles and hybrid vehicles, or servo motors for robots and machine tools, and its industrial value and contribution to the industry are high.
- the tensile strength increases with the addition of Ti, but the effect is small in the region A in FIG. 1 where the addition amount is small, and stable in the Ti amount range shown in the region B in the drawing. As a result, the strength was improved. Further, in the region C in the figure where the Ti amount is high, the strength further increases.
- the steel structure in region B had a uniform microstructure with a crystal grain size of 10 ⁇ m or less, whereas the crystal grains in the steel structure in region A grew from region B. In particular, it exhibited a mixed grain structure in which partial grain growth was observed.
- the region C a composite structure of non-recrystallized grains and recrystallized grains was exhibited.
- FIG. 2 shows the relationship between the Ti addition amount and the iron loss W 10/400 .
- the iron loss is the lowest and good, but as shown in FIG. 1, the region A has a low strength level.
- regions C and D in the figure a high-strength material is obtained, but the iron loss is also high.
- the region B a material that has a strength comparable to that of the region C and has good iron loss close to that of the region A is obtained.
- hege defects begin to increase when the Ti addition amount exceeds 0.04%, and increases until the element equivalent ratio of Ti, C, and N becomes 1, and there is a substantially constant hege defect. It has reached the amount of galling. If the C and N contents are constant, the precipitation amount of Ti carbonitride increases until the element equivalent ratio becomes 1, and thereafter, the precipitation amount becomes constant. The amount is considered to be related to the amount of balding. From these results, by controlling the amount of Ti added to the range of region B, high strength and low iron are achieved while suppressing whisker defects that directly cause an increase in manufacturing cost which causes a decrease in yield and troubles in sheet breakage. It became clear that it was possible to balance losses. That is, it is understood that Ti needs an amount to form a certain amount of Ti carbonitride, but it is advantageous to contain Ti at 0.04% or less from the viewpoint of suppressing hege defects.
- steels b, c, and d have increased strength, but by comparing steels c and d in which the total amount of C and N is approximately the same, the effect of addition of C and N is The steel c having a lower amount has higher strength.
- the order of crystal grain size was steel a>d>b> c, corresponding to the order of tensile strength.
- the test conditions were a tension-tensile mode with a stress ratio of 0.1, a cycle of 20 Hz, and a stress that did not break at an amplitude of 10 million times as fatigue limit strength.
- the results are also shown in Table 2.
- the material with higher tensile strength TS tends to have higher fatigue limit strength FS, but the ratio FS / TS is different, and steel c is the most excellent result.
- steel d has a small improvement margin for fatigue limit strength despite its high tensile strength. Therefore, when the structure of steel d was investigated in detail, it was presumed that precipitates thought to be TiN exceeding a particle size of 5 ⁇ m were scattered, and this was the starting point of fatigue fracture.
- nitrogen reacts with Ti at a relatively high temperature of 1100 ° C. or more and is likely to precipitate coarsely as TiN. Therefore, TiN is likely to be a starting point of fatigue fracture, and compared with Ti carbide, it is considered that the effect of suppressing grain growth, which is one of the aims of the present invention, is small.
- steel c is superior in both tensile strength and fatigue limit strength, but in particular, fatigue limit strength is relatively high and strength ratio FS / TS is high. It is characteristic. Since the Ti and N contents of steels b and c are almost the same, the precipitation of Ti nitride and Ti carbide is the same, and the difference between the two is considered to be due to the difference in the amount of solute carbon. . Therefore, it is presumed that the presence of solute carbon suppresses the generation and propagation of cracks and increases the fatigue limit strength by fixing dislocations introduced under repeated stress as in a fatigue test. Therefore, it is important to secure solid solution carbon.
- Si 5.0% or less
- Mn 2.0% or less
- Al 2.0% or less
- P 0.05% or less are contained within a range satisfying the following formula (1). 300 ⁇ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ⁇ 430 (1)
- the purpose of the present invention is to provide a magnetic steel sheet having high strength and excellent magnetic properties at low cost, and for this purpose, the amount of solid solution strengthening by the above four main alloy components needs to be a certain level or more. Therefore, in addition to defining the individual contents of the main four alloy components as described below, the total amount of the main four alloy components is as described above in consideration of the contribution to the individual solid solution strengthening amounts. It is important to add in a range satisfying the formula (1). That is, if the formula (1) is less than 300, the resulting material strength is insufficient. On the other hand, if it exceeds 430, troubles in plate cracking at the time of steel plate production increase, resulting in a decrease in productivity and a significant increase in production cost.
- Si 5.0% or less
- Si is a main element constituting a non-oriented electrical steel sheet that has the effect of increasing the electrical resistance of steel and reducing iron loss. Furthermore, it has a high solid solution strengthening ability. In other words, compared to other solid solution strengthening elements such as Mn, Al, and Ni added to non-oriented electrical steel sheets, it is possible to achieve both high tensile strength, high fatigue strength and low iron loss in the most balanced manner. Since it is an element that can be produced, it is an element that is actively added. For that purpose, it is advantageous to contain it at 3.0% or more, more preferably more than 3.5%. However, if it exceeds 5.0%, toughness deterioration becomes remarkable, and advanced control is required at the time of sheet passing and rolling, and productivity is also lowered. Therefore, the upper limit is 5.0% or less.
- Mn 2.0% or less
- Mn In addition to being effective in improving hot brittleness, Mn also has the effect of increasing the electrical resistance of steel to reduce iron loss and the effect of improving strength by solid solution strengthening. Therefore, it is preferable to contain Mn 0.01% or more. However, Mn has a lower strength improvement effect than Si, and excessive addition causes embrittlement of the steel, so the Mn content is 2.0% or less.
- Al is an element generally used in steel refining as a powerful deoxidizer. Furthermore, like Si and Mn, it has the effect of increasing the electrical resistance of steel to reduce iron loss and the effect of improving strength by solid solution strengthening. Accordingly, Al is preferably contained in an amount of 0.0001% or more. However, Al has a smaller strength improvement effect than Si, and excessive addition causes embrittlement of the steel, so the Al content is 2.0% or less.
- P 0.05% or less P is extremely effective for increasing the strength because a significant solid solution strengthening ability can be obtained even when added in a relatively small amount, and is preferably contained at 0.005% or more.
- the addition amount is limited to 0.05% or less.
- an alloy design mainly composed of Si is advantageous in order to achieve the most efficient combination of solid solution strengthening, low iron loss and manufacturability. That is, it is advantageous to contain Si in the range of more than 3.5% in order to optimize the characteristic balance of the non-oriented electrical steel sheet.
- the remaining three components are Mn: 0.3% or less and Al: It is preferable to regulate to 0.1% or less and P: 0.05% or less. The reason for this upper limit is the same as described above.
- C 0.008% or more and 0.040% or less C needs to be 0.008% or more. That is, if it is less than 0.008%, it becomes difficult to precipitate fine Ti carbide stably, and since the amount of solute C is insufficient, further improvement in fatigue strength cannot be expected. On the other hand, excessive addition leads to deterioration of magnetic characteristics, and work hardening during cold rolling becomes significant, causing plate breakage, and increased rolling load due to increased rolling load. This limits the upper limit to 0.04%.
- N forms Ti and nitride, but is not so effective for refinement of crystal grains because it is produced at a higher temperature than Ti carbide and has a weak effect of suppressing crystal grain growth. Rather, it may be adversely affected such as starting from fatigue failure, so it is limited to 0.003% or less.
- it does not specifically limit about a minimum, It is preferable to set it as about 0.0005% from a viewpoint of the steelmaking degassing capability and productivity fall by long-time refining.
- Ti 0.04% or less
- Ti amount capable of forming carbide is expressed as Ti *
- Ti * ⁇ 0.008 is necessary together with an appropriate amount of C.
- the Ti addition amount is increased with respect to the C amount, the solid solution C decreases and the effect of improving the fatigue strength cannot be expected. Therefore, it is necessary to satisfy Ti * ⁇ 1.2 [C%] at the same time.
- Sb and Sn effective in improving magnetic properties are 0.0005 to 0.1%
- B effective in increasing grain boundary strength is 0.0005 to 0.01%
- the effect of improving magnetic properties by controlling the form of oxides and sulfides Ca and REM with a content of 0.001 to 0.01%
- Co and Ni with an effect of improving the magnetic flux density of 0.05 to 5%
- Cu with the potential for precipitation strengthening due to aging precipitation may be added in a range of 0.2 to 4%. Is possible.
- the manufacturing process from steel melting to cold rolling can be implemented according to the method currently performed with the general non-oriented electrical steel sheet.
- steel that has been melted and refined to a specified component in a converter or electric furnace is made into a steel slab by continuous casting or ingot rolling after ingot forming, hot rolling, hot-rolled sheet annealing as needed, cold It can be manufactured through processes such as cold rolling, finish annealing, and insulating film coating and baking.
- the conditions for properly controlling the precipitation state are as follows.
- after hot rolling it is possible to perform hot-rolled sheet annealing as necessary, and cold rolling may be performed once or twice or more with intermediate annealing interposed therebetween.
- Slab heating temperature when hot-rolling a steel slab having the above-described composition is set to 1000 ° C. or more and 1200 ° C. or less. That is, when the temperature is lower than 1000 ° C., Ti carbide precipitates and grows during slab heating, so that the effect of suppressing crystal grain growth during finish annealing cannot be sufficiently exhibited. On the other hand, if it exceeds 1200 ° C, in addition to being disadvantageous in terms of cost, the operability is deteriorated, for example, the high-temperature strength is lowered and the slab is deformed to hinder extraction from the heating furnace. Accordingly, the slab heating temperature is set to 1000 ° C. or more and 1200 ° C. or less.
- the hot rolling itself is not particularly limited.
- the hot rolling finishing temperature can be set to 700 to 950 ° C.
- the winding temperature can be set to 750 ° C. or less.
- finish annealing is performed.
- the said heat processing it is preferable to perform the said heat processing to serve as either hot-rolled sheet annealing or intermediate annealing prior to finish annealing.
- finish annealing is performed at 700 ° C. or higher and 850 ° C. or lower, whereby a recrystallized grain structure can be controlled uniformly and finely to obtain an electrical steel sheet having high strength and excellent magnetic properties.
- finish annealing temperature is less than 700 ° C., recrystallization becomes insufficient.
- 850 ° C. crystal grains are likely to grow even when the present invention is applied, and the strength is lowered.
- an insulating film is applied and baked to obtain a final product.
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Abstract
Description
そして、本発明は、上記の無方向性電磁鋼板を、従来よりも低コストで提供するものである。 The present invention is a non-oriented electrical steel sheet, particularly a component subjected to a large stress such as a rotor of a high-speed rotating machine, such as a drive motor of a turbine generator, an electric vehicle and a hybrid vehicle, or a servo motor of a robot or a machine tool. The present invention relates to a non-oriented electrical steel sheet having high strength, excellent fatigue characteristics and excellent magnetic characteristics, and a method for producing the same.
And this invention provides said non-oriented electrical steel sheet at lower cost than before.
ここに、固溶強化を活用したものとして、例えば特許文献1には、Si含有量を3.5~7.0%と高めることを基本として、さらに固溶強化のためにTi,W,Mo,Mn,Ni,CoおよびAlなどの元素を添加して高強度化を図る方法が提案されている。さらに、特許文献2には、上記強化法に加え、仕上げ焼鈍条件の工夫により結晶粒径を0.01~5.0mmに制御して磁気特性を改善する方法が提案されている。 Steel strengthening mechanisms include solid solution strengthening, precipitation strengthening, grain refinement, and work hardening. Up to now, high-strength non-oriented electrical steel sheets that meet the needs of high-speed rotating motor rotors have been developed. Some considerations and suggestions have been made.
Here, for example, in
同様に、特許文献4には、前記特許文献3に記載された事項に加えて、NiおよびMnを合計で0.3%以上10%以下添加して固溶強化した上で、前記特許文献3に記載されたと同様の比率のNb、Zr、TiおよびVを添加して、高強度並びに磁気特性の両立をはかる技術が提案されている。 In addition, as a technique using precipitation of carbonitride, Patent Document 3 discloses that in a steel having an Si content of 2.0% or more and less than 4.0%, C is set to 0.05% or less, and among Nb, Zr, Ti, and V, Carbonitride containing 1 or 2 in the range of 0.1 <(Nb + Zr) / 8 (C + N) <1.0, 0.4 <(Ti + V) / 4 (C + N) <4.0 A technique that utilizes precipitation strengthening and grain refinement effects due to slag has been proposed.
Similarly, in Patent Document 4, in addition to the matters described in Patent Document 3, Ni and Mn are added in a total solution of 0.3% or more and 10% or less to enhance the solid solution, and then described in Patent Document 3. A technique has been proposed in which Nb, Zr, Ti and V are added in the same ratio as described above to achieve both high strength and magnetic properties.
すなわち、本発明は以下の知見に立脚するものである。
(イ)比較的少量のTi炭化物の存在により、電磁鋼板の仕上げ焼鈍における結晶粒の成長は抑制でき、結晶粒の微細化による強化が図れること。
(ロ)Ti炭化物の量が多すぎても結晶粒成長の抑制効果には寄与しないばかりか、表面欠陥や内部欠陥が増加し鋼板品質が低下したり、破壊起点となる等の悪影響をもたらすこと。この点、Tiの添加を適正範囲に制御することにより、ヘゲなどの表面欠陥や内部欠陥は大幅に減少すること。
一方、Ti窒化物はTi炭化物より高温で生成するため、結晶粒成長を抑制する効果が弱く、本発明の目的とする結晶粒の微細化制御には有用でないこと。従って、Ti炭化物量を制御することで結晶粒成長を抑制する手法においては、Nは安定的に低減することが望ましいこと。これは、CおよびNの効果が同様に扱われている従来の析出強化手法とは全く異なるものである。
(ハ)結晶粒を微細化した鋼板において、固溶Cは、引張強さを高めるだけでなく、高速回転するロータ材に本質的に必要である疲労特性を向上させる効果を有すること。
(ニ)電磁鋼板の電気抵抗を高めて低鉄損化を図る目的にて通常添加されている主要合金成分はSi,AlおよびMnの3元素であるが、これらの置換型合金元素には鋼を固溶強化する効果もある。従って、高強度と低鉄損を両立するためには、これらの元素による固溶強化をベースとするのが有効であること。一方、これらの元素の過剰添加は鋼を脆化して製造が困難になるため、添加には限界があり、固溶強化、低鉄損化および製造性の3点を、最も効率良く充足するには、Siを主体とした添加が望ましいこと。 The inventors conducted various studies on a high-strength electrical steel sheet that can achieve the above-described object at a high level and a method for manufacturing the same. As a result, it has been found that the addition amount and addition ratio of Ti and C are deeply involved in the balance of strength and magnetic properties of the electrical steel sheet, and by optimizing the precipitation amount of Ti carbide, high strength with excellent properties It was found that electrical steel sheets can be manufactured stably and at low cost.
That is, the present invention is based on the following knowledge.
(A) The presence of a relatively small amount of Ti carbide can suppress the growth of crystal grains in the final annealing of electrical steel sheets, and can be strengthened by refinement of crystal grains.
(B) Too much Ti carbide not only contributes to the effect of suppressing grain growth, but also causes adverse effects such as increased surface defects and internal defects, resulting in decreased steel sheet quality and a starting point for fracture. . In this regard, by controlling the addition of Ti to an appropriate range, surface defects such as scabs and internal defects should be greatly reduced.
On the other hand, since Ti nitride is produced at a higher temperature than Ti carbide, the effect of suppressing crystal grain growth is weak, and it is not useful for controlling grain refinement, which is the object of the present invention. Therefore, it is desirable that N is stably reduced in a method for suppressing grain growth by controlling the amount of Ti carbide. This is quite different from the conventional precipitation strengthening technique in which the effects of C and N are treated similarly.
(C) In a steel plate with refined crystal grains, the solid solution C not only increases the tensile strength, but also has the effect of improving the fatigue characteristics that are essentially necessary for a rotor material that rotates at high speed.
(D) The main alloy components usually added for the purpose of increasing the electric resistance of the electrical steel sheet and reducing the iron loss are three elements of Si, Al and Mn. There is also an effect of strengthening solid solution. Therefore, in order to achieve both high strength and low iron loss, it is effective to base on solid solution strengthening with these elements. On the other hand, excessive addition of these elements embrittles steel and makes it difficult to manufacture. Therefore, there is a limit to the addition, and the three points of solid solution strengthening, low iron loss and manufacturability are most efficiently satisfied. It is desirable to add mainly Si.
(i)質量%で、
Si:5.0%以下、
Mn:2.0%以下、
Al:2.0%以下および
P:0.05%以下
を、下記式(1)を満足する範囲において含み、さらに
C:0.008%以上0.040%以下、
N:0.003%以下および
Ti:0.04%以下
を、下記式(2)を満足する範囲において含有し、残部はFeおよび不可避的不純物からなることを特徴とする無方向性電磁鋼板。
記
300≦85[Si%]+16[Mn%]+40[Al%]+490[P%]≦430 …(1)
0.008≦Ti*<1.2[C%] …(2)
但し、Ti*=Ti-3.4[N%]
ここで、前記[Si%]、[Mn%]、[Al%]、[P%]、[C%]および[N%]は、それぞれ表示元素の含有量(質量%)を示す。 That is, the gist of the present invention is as follows.
(I)% by mass
Si: 5.0% or less,
Mn: 2.0% or less,
Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less,
A non-oriented electrical steel sheet containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2), the balance being Fe and inevitable impurities.
300 ≦ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ≦ 430 (1)
0.008 ≦ Ti * <1.2 [C%] (2)
However, Ti * = Ti-3.4 [N%]
Here, [Si%], [Mn%], [Al%], [P%], [C%], and [N%] each indicate the content (% by mass) of the display element.
Si:3.5%超5.0%以下、
Mn:0.3%以下、
Al:0.1%以下および
P:0.05%以下
であることを特徴とする無方向性電磁鋼板。 (Ii) In the above (i), the contents of Si, Mn, Al and P are mass%,
Si: more than 3.5% and less than 5.0%
Mn: 0.3% or less,
A non-oriented electrical steel sheet characterized by Al: 0.1% or less and P: 0.05% or less.
Sb:0.0005%以上0.1%以下、
Sn:0.0005%以上0.1%以下、
B:0.0005%以上0.01%以下、
Ca:0.001%以上0.01%以下、
REM:0.001%以上0.01%以下、
Co:0.05%以上5%以下、
Ni:0.05%以上5%以下および
Cu:0.2%以上4%以下
の1種または2種以上を含むことを特徴とする無方向性電磁鋼板。 (Iii) In the above (i) or (ii), Sb: 0.0005% to 0.1% in mass%,
Sn: 0.0005% to 0.1%,
B: 0.0005% or more and 0.01% or less,
Ca: 0.001% to 0.01%,
REM: 0.001% to 0.01%,
Co: 0.05% or more and 5% or less,
A non-oriented electrical steel sheet comprising one or more of Ni: 0.05% to 5% and Cu: 0.2% to 4%.
Si:5.0%以下、
Mn:2.0%以下、
Al:2.0%以下および
P:0.05%以下
を、下記式(1)を満足する範囲において含み、さらに
C:0.008%以上0.040%以下、
N:0.003%以下および
Ti:0.04%以下
を、下記式(2)を満足する範囲において含有する、鋼スラブを、1000~1200℃で均熱保持した後熱間圧延し、次いで1回または中間焼鈍を挟む2回以上の冷間圧延または温間圧延にて最終板厚とした後、仕上げ焼鈍を施すに当たり、前記仕上げ焼鈍に先立ち、800℃以上950℃以下の温度に30秒以上保持する熱処理を少なくとも1回は施し、その後、仕上げ焼鈍を700℃以上850℃以下で行うことを特徴とする無方向性電磁鋼板の製造方法。
記
300≦85[Si%]+16[Mn%]+40[Al%]+490[P%]≦430 …(1)
0.008≦Ti*<1.2[C%] …(2)
但し、Ti*=Ti-3.4[N%] (Iv)% by mass
Si: 5.0% or less,
Mn: 2.0% or less,
Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less,
A steel slab containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2) is kept hot at 1000 to 1200 ° C. and then hot-rolled, and then once or in the middle Heat treatment is performed at a temperature of 800 ° C or higher and 950 ° C or lower for 30 seconds or more prior to the final annealing before the final annealing after the final thickness is obtained by cold rolling or warm rolling at least twice with annealing. Is applied at least once, and then finish annealing is performed at 700 ° C. or higher and 850 ° C. or lower.
300 ≦ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ≦ 430 (1)
0.008 ≦ Ti * <1.2 [C%] (2)
However, Ti * = Ti-3.4 [N%]
Si:3.5%超5.0%以下、
Mn:0.3%以下、
Al:0.1%以下および
P:0.05%以下
であることを特徴とする無方向性電磁鋼板の製造方法。 (V) In (iv), the contents of Si, Mn, Al, and P are mass%,
Si: more than 3.5% and less than 5.0%
Mn: 0.3% or less,
A method for producing a non-oriented electrical steel sheet, wherein Al: 0.1% or less and P: 0.05% or less.
Sb:0.0005%以上0.1%以下、
Sn:0.0005%以上0.1%以下、
B:0.0005%以上0.01%以下、
Ca:0.001%以上0.01%以下、
REM:0.001%以上0.01%以下、
Co:0.05%以上5%以下、
Ni:0.05%以上5%以下および
Cu:0.2%以上4%以下
の1種または2種以上を含むことを特徴とする無方向性電磁鋼板の製造方法。 (Vi) In the above (iv) or (v), in addition, by mass%, Sb: 0.0005% or more and 0.1% or less,
Sn: 0.0005% to 0.1%,
B: 0.0005% or more and 0.01% or less,
Ca: 0.001% to 0.01%,
REM: 0.001% to 0.01%,
Co: 0.05% or more and 5% or less,
A method for producing a non-oriented electrical steel sheet, comprising one or more of Ni: 0.05% to 5% and Cu: 0.2% to 4%.
すなわち、発明者らは、主要な炭窒化物形成元素であるTiが、析出強化、再結晶、粒成長挙動およびヘゲなどの鋼板品質に及ぼす影響について詳細に検討した。その結果、Tiは、特にCやNに対して原子当量以下の範囲で添加した場合の効果が大きく異なり、高強度とともに磁気特性や鋼板品質を高い次元で満足するための最適添加範囲が存在することがわかった。その主要な実験結果を示す。なお、以下に示す「%」の表示は、特に断らない限り、「質量%」を意味する。 Hereinafter, the experiment that led to the present invention will be described in detail.
That is, the inventors examined in detail the influence of Ti, which is the main carbonitride-forming element, on the steel plate quality such as precipitation strengthening, recrystallization, grain growth behavior, and baldness. As a result, especially when Ti is added in a range of not more than atomic equivalent to C and N, the effect is greatly different, and there is an optimum addition range for satisfying magnetic properties and steel plate quality at a high level as well as high strength. I understood it. The main experimental results are shown. In addition, unless otherwise indicated, the display of "%" shown below means "mass%".
Si:4.0~4.1%、Mn:0.03~0.05%、Al:0.001%以下、P:0.007~0.009%およびS:0.001~0.002%を主要成分として、C量を0.024~0.026%、N量を0.001~0.002%とほぼ一定量で含む鋼組成において、Ti量を0.001~0.36%の範囲に変化させた鋼を真空溶解炉で種々溶製し、1100℃に加熱後熱間圧延によって2.1mm厚とした。その後900℃で90秒の熱延板焼鈍を行い、さらに冷間圧延により0.35mm厚とした後、鋼板表面のヘゲ欠陥発生状況(単位面積当たりのヘゲ長さ)を評価した。その後800℃で30秒の仕上げ焼鈍を施し、機械特性(圧延方向と平行にJIS5号試験片を切り出し評価)および磁気特性(圧延平行方向と圧延直角方向にエプスタイン試験片を切り出し、励磁磁束密度1.0T、周波数400Hzにおける鉄損W10/400を測定)を評価した。Ti量と引張り強さ、磁気特性、表面ヘゲ欠陥発生に関する調査結果を、図1、図2および図3に示す。 <
Si: 4.0-4.1%, Mn: 0.03-0.05%, Al: 0.001% or less, P: 0.007-0.009% and S: 0.001-0.002% as main components, C amount is 0.024-0.026%, N amount is 0.001 In steel composition containing approximately constant amount of up to 0.002%, various steels with Ti content changed in the range of 0.001 to 0.36% were melted in a vacuum melting furnace, heated to 1100 ° C and hot rolled to 2.1mm thickness did. Thereafter, hot-rolled sheet annealing was performed at 900 ° C. for 90 seconds, and the thickness was further reduced to 0.35 mm by cold rolling, and then the state of occurrence of shave defects on the surface of the steel sheet (shave length per unit area) was evaluated. Then, finish annealing is performed at 800 ° C for 30 seconds, and mechanical characteristics (JIS5 test piece is cut out in parallel with the rolling direction and evaluated) and magnetic properties (Epstein test piece are cut out in the rolling parallel direction and perpendicular to the rolling direction). T, iron loss W 10/400 at a frequency of 400 Hz was measured). The investigation results on the Ti content, tensile strength, magnetic properties, and surface bald defects are shown in FIG. 1, FIG. 2 and FIG.
これらの結果から、Ti添加量を領域Bの範囲に制御することにより、歩留まりの低下や板破断トラブルの原因となり製造コストの増加に直結する、ヘゲ欠陥を抑制しつつ、高強度と低鉄損を両立可能であることが明らかとなった。すなわち、Tiはある程度のTi炭窒化物を形成する量が必要であるが、ヘゲ欠陥の抑制の観点から0.04%以下で含有するのが有利であることがわかる。 On the other hand, as shown in FIG. 3, hege defects begin to increase when the Ti addition amount exceeds 0.04%, and increases until the element equivalent ratio of Ti, C, and N becomes 1, and there is a substantially constant hege defect. It has reached the amount of galling. If the C and N contents are constant, the precipitation amount of Ti carbonitride increases until the element equivalent ratio becomes 1, and thereafter, the precipitation amount becomes constant. The amount is considered to be related to the amount of balding.
From these results, by controlling the amount of Ti added to the range of region B, high strength and low iron are achieved while suppressing whisker defects that directly cause an increase in manufacturing cost which causes a decrease in yield and troubles in sheet breakage. It became clear that it was possible to balance losses. That is, it is understood that Ti needs an amount to form a certain amount of Ti carbonitride, but it is advantageous to contain Ti at 0.04% or less from the viewpoint of suppressing hege defects.
次に、Ti炭窒化物の影響を詳細に調査するため、表1に示す組成の鋼を真空溶解炉で溶製し、実験1と同様の手順で板厚0.35mmの鋼板を作製した。CおよびN量がともに少ない鋼aをベースとして、CおよびN量を変化させた。鋼cおよびdは、C+N量が一定となるように添加したものである。得られた試料の表面ヘゲ欠陥率、鉄損、引張強さを表2に示す。鋼aに対して、鋼b、cおよびdは強度が上昇しているが、CおよびNの合計量がほぼ同等の鋼cおよびdの比較により、CおよびNの添加効果を見ると、N量が低い鋼cの方がより高強度である。組織観察したところ結晶粒径の序列は、鋼a>d>b>cであり、引張強さの序列と対応していた。 <Experiment 2>
Next, in order to investigate the influence of Ti carbonitride in detail, steel having the composition shown in Table 1 was melted in a vacuum melting furnace, and a steel plate having a thickness of 0.35 mm was produced in the same procedure as in
まず、主要な鋼成分の限定理由について説明する。
Si:5.0%以下、Mn:2.0%以下、Al:2.0%以下およびP:0.05%以下を、下記式(1)を満足する範囲において含有する。
記
300≦85[Si%]+16[Mn%]+40[Al%]+490[P%]≦430 …(1) Next, the present invention will be described in detail for each requirement.
First, the reasons for limiting the main steel components will be described.
Si: 5.0% or less, Mn: 2.0% or less, Al: 2.0% or less, and P: 0.05% or less are contained within a range satisfying the following formula (1).
300 ≦ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ≦ 430 (1)
Si:5.0%以下
Siは、脱酸剤として一般的に用いられる他、鋼の電気抵抗を高めて鉄損を低減する効果を有する、無方向性電磁鋼板を構成する主要元素である。さらに、高い固溶強化能を有する。すなわち、無方向性電磁鋼板に添加されるMn、AlおよびNiなど、他の固溶強化元素と比較して、高抗張力化、高疲労強度化並びに低鉄損化を最もバランス良く両立することが出来る元素であるため、積極的に添加する元素である。そのためには、3.0%以上で含有させること、さらに好ましくは3.5%を超えて含有させることが有利である。しかしながら、5.0%を超えると、靭性劣化が顕著になり、通板および圧延時に高度な制御が必要となり生産性も低下する。よって、上限は5.0%以下とする。 Next, the reason for limiting the content of each of the four main alloy components will be described.
Si: 5.0% or less In addition to being generally used as a deoxidizer, Si is a main element constituting a non-oriented electrical steel sheet that has the effect of increasing the electrical resistance of steel and reducing iron loss. Furthermore, it has a high solid solution strengthening ability. In other words, compared to other solid solution strengthening elements such as Mn, Al, and Ni added to non-oriented electrical steel sheets, it is possible to achieve both high tensile strength, high fatigue strength and low iron loss in the most balanced manner. Since it is an element that can be produced, it is an element that is actively added. For that purpose, it is advantageous to contain it at 3.0% or more, more preferably more than 3.5%. However, if it exceeds 5.0%, toughness deterioration becomes remarkable, and advanced control is required at the time of sheet passing and rolling, and productivity is also lowered. Therefore, the upper limit is 5.0% or less.
Mnは、熱間脆性の改善に有効であることに加え、鋼の電気抵抗を高めて鉄損を低減する効果、固溶強化による強度向上効果も有する。従って、Mnは0.01%以上含有させることが好ましい。ただし、MnはSiと比べると強度向上効果は小さく、過度の添加は鋼の脆化を招くため、Mn量は2.0%以下とする。 Mn: 2.0% or less In addition to being effective in improving hot brittleness, Mn also has the effect of increasing the electrical resistance of steel to reduce iron loss and the effect of improving strength by solid solution strengthening. Therefore, it is preferable to contain Mn 0.01% or more. However, Mn has a lower strength improvement effect than Si, and excessive addition causes embrittlement of the steel, so the Mn content is 2.0% or less.
Alは、強力な脱酸剤として鋼精錬に一般的に用いられる元素である。さらに、SiやMnと同様に、鋼の電気抵抗を高めて鉄損を低減する効果、固溶強化による強度向上効果も有する。従って、Alは0.0001%以上含有させることが好ましい。ただし、AlはSiと比べると強度向上効果は小さく、過度の添加は鋼の脆化を招くため、Al量は2.0%以下とする。 Al: 2.0% or less Al is an element generally used in steel refining as a powerful deoxidizer. Furthermore, like Si and Mn, it has the effect of increasing the electrical resistance of steel to reduce iron loss and the effect of improving strength by solid solution strengthening. Accordingly, Al is preferably contained in an amount of 0.0001% or more. However, Al has a smaller strength improvement effect than Si, and excessive addition causes embrittlement of the steel, so the Al content is 2.0% or less.
Pは、比較的少量の添加でも大幅な固溶強化能が得られるため、高強度化に極めて有効であり、好ましくは0.005%以上で含有させる。しかし、過剰な添加は偏析による脆化により粒界割れや圧延性の低下をもたらすため、その添加量を0.05%以下に制限する。 P: 0.05% or less P is extremely effective for increasing the strength because a significant solid solution strengthening ability can be obtained even when added in a relatively small amount, and is preferably contained at 0.005% or more. However, excessive addition leads to grain boundary cracking and rollability deterioration due to embrittlement due to segregation, so the addition amount is limited to 0.05% or less.
記
0.008≦Ti*<1.2[C%] …(2)
但し、Ti*=Ti-3.4[N%] C, N and Ti are also important elements in the present invention. This is because it is important to suppress the grain growth during annealing of the steel sheet by using an appropriate amount of fine Ti carbide to develop the strengthening of grain refinement. For that purpose, it is necessary to contain C: 0.008% or more and 0.040% or less, N: 0.003% or less, and Ti: 0.04% or less in a range satisfying the following formula (2).
0.008 ≦ Ti * <1.2 [C%] (2)
However, Ti * = Ti-3.4 [N%]
Cは、0.008%以上が必要である。すなわち、0.008%未満では安定して微細Ti炭化物を析出させることが困難となり、また固溶C量が不足してしまうために疲労強度の一層の向上が見込めなくなる。一方、過度の添加は磁気特性の劣化をもたらすと共に、冷間圧延中の加工硬化が著しくなって板破断の原因となったり、圧延負荷の増大で圧延回数の増加が余儀なくされるなど、コスト上昇の要因となるため、上限を0.04%に規制する。 C: 0.008% or more and 0.040% or less C needs to be 0.008% or more. That is, if it is less than 0.008%, it becomes difficult to precipitate fine Ti carbide stably, and since the amount of solute C is insufficient, further improvement in fatigue strength cannot be expected. On the other hand, excessive addition leads to deterioration of magnetic characteristics, and work hardening during cold rolling becomes significant, causing plate breakage, and increased rolling load due to increased rolling load. This limits the upper limit to 0.04%.
Nは、Tiと窒化物を形成するが、Ti炭化物より高温で生成し結晶粒成長を抑制する効果が弱いため、結晶粒の微細化のためにはそれほど有効ではない。むしろ疲労破壊起点になるなどの悪影響を及ぼす場合もあるため、0.003%以下に限定する。なお、下限については、特に限定するものではないが、製鋼脱ガス能力、長時間精錬による生産性低下の観点から、0.0005%程度とすることが好ましい。 N: 0.003% or less N forms Ti and nitride, but is not so effective for refinement of crystal grains because it is produced at a higher temperature than Ti carbide and has a weak effect of suppressing crystal grain growth. Rather, it may be adversely affected such as starting from fatigue failure, so it is limited to 0.003% or less. In addition, although it does not specifically limit about a minimum, It is preferable to set it as about 0.0005% from a viewpoint of the steelmaking degassing capability and productivity fall by long-time refining.
本発明において、Ti炭化物を制御することは重要である。Tiは、炭化物を形成するよりも高温で窒化物を形成しやすいため、炭化物を形成するTi量を制御する必要がある。ここに、炭化物の形成が可能なTi量をTi*と表すと、このTi*は、Ti含有量からNとの原子当量分を除いた量、すなわち
Ti*=Ti-3.4[N%]
と表される。添加するTiをTi炭化物として析出させて高強度化を図りつつ、結晶粒成長を抑制させて鉄損の増大を防ぐには、適量のCと共に、Ti*≧0.008が必要である。一方、C量に対してTi添加量が増加すると、固溶Cが減少し疲労強度を向上させる効果が見込めなくなるため、Ti*<1.2[C%]も同時に満たすことが必要である。 Ti: 0.04% or less In the present invention, it is important to control Ti carbide. Since Ti tends to form nitride at a higher temperature than that of carbide, it is necessary to control the amount of Ti that forms carbide. Here, when Ti amount capable of forming carbide is expressed as Ti *, this Ti * is an amount obtained by subtracting an atomic equivalent of N from Ti content, that is, Ti * = Ti−3.4 [N%].
It is expressed. In order to suppress the growth of crystal grains and prevent an increase in iron loss while precipitating Ti to be added as Ti carbide to increase the strength, Ti * ≧ 0.008 is necessary together with an appropriate amount of C. On the other hand, if the Ti addition amount is increased with respect to the C amount, the solid solution C decreases and the effect of improving the fatigue strength cannot be expected. Therefore, it is necessary to satisfy Ti * <1.2 [C%] at the same time.
本発明において、鋼溶製から冷間圧延までの製造工程は、一般的な無方向性電磁鋼板で行われている方法に従って実施することが出来る。例えば、転炉あるいは電気炉などで所定成分に溶製、精錬された鋼を、連続鋳造あるいは造塊後の分塊圧延により鋼スラブとし、熱間圧延、必要に応じて熱延板焼鈍、冷間圧延、仕上げ焼鈍、絶縁被膜塗布焼き付け、といった工程を経て製造することが出来る。これらの工程において、析出状態を適正に制御するための条件は次のとおりである。なお、熱間圧延後に、必要に応じて熱延板焼鈍を施すことが可能であり、冷間圧延は、1回または中間焼鈍を挟む2回以上で行ってもよい。 Next, the reasons for limiting the manufacturing method will be described.
In this invention, the manufacturing process from steel melting to cold rolling can be implemented according to the method currently performed with the general non-oriented electrical steel sheet. For example, steel that has been melted and refined to a specified component in a converter or electric furnace is made into a steel slab by continuous casting or ingot rolling after ingot forming, hot rolling, hot-rolled sheet annealing as needed, cold It can be manufactured through processes such as cold rolling, finish annealing, and insulating film coating and baking. In these steps, the conditions for properly controlling the precipitation state are as follows. In addition, after hot rolling, it is possible to perform hot-rolled sheet annealing as necessary, and cold rolling may be performed once or twice or more with intermediate annealing interposed therebetween.
なお、式(1)の値が本発明の範囲を外れる鋼18は、冷間圧延で板割れが生じたため、以降の評価は行っていない。 Steels having the compositions shown in Table 5 were melted in a vacuum melting furnace, heated to 1050 ° C. and hot-rolled to 2.1 mm thickness. Thereafter, hot-rolled sheet annealing was performed at 850 ° C. for 120 seconds, and the thickness was further reduced to 0.35 mm by cold rolling. The state of occurrence of shave defects on the steel sheet surface obtained here was evaluated using the shave length per unit area as an index. Thereafter, finish annealing was performed at 800 ° C. for 30 seconds, and a test piece was cut out in parallel to the rolling direction for the obtained sample, and a tensile test and a fatigue test were performed. Further, the magnetic properties were evaluated by iron loss at an excitation magnetic flux density of 1.0 T and a frequency of 400 Hz after cutting out Epstein test pieces in the rolling parallel direction and the rolling perpendicular direction. The results are also shown in Table 6.
In addition, since the steel 18 which the value of Formula (1) remove | deviates from the range of this invention has produced the plate crack by cold rolling, subsequent evaluation is not performed.
Claims (6)
- 質量%で、
Si:5.0%以下、
Mn:2.0%以下、
Al:2.0%以下および
P:0.05%以下
を、下記式(1)を満足する範囲において含み、さらに
C:0.008%以上0.040%以下、
N:0.003%以下および
Ti:0.04%以下
を、下記式(2)を満足する範囲において含有し、残部はFeおよび不可避的不純物からなることを特徴とする無方向性電磁鋼板。
記
300≦85[Si%]+16[Mn%]+40[Al%]+490[P%]≦430 …(1)
0.008≦Ti*<1.2[C%] …(2)
但し、Ti*=Ti-3.4[N%] % By mass
Si: 5.0% or less,
Mn: 2.0% or less,
Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less,
A non-oriented electrical steel sheet containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2), the balance being Fe and inevitable impurities.
300 ≦ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ≦ 430 (1)
0.008 ≦ Ti * <1.2 [C%] (2)
However, Ti * = Ti-3.4 [N%] - 請求項1において、Si、Mn、AlおよびPの含有量が、質量%で、
Si:3.5%超5.0%以下、
Mn:0.3%以下、
Al:0.1%以下および
P:0.05%以下
であることを特徴とする無方向性電磁鋼板。 In Claim 1, content of Si, Mn, Al, and P is the mass%,
Si: more than 3.5% and less than 5.0%
Mn: 0.3% or less,
A non-oriented electrical steel sheet characterized by Al: 0.1% or less and P: 0.05% or less. - 請求項1または2において、さらに、質量%で
Sb:0.0005%以上0.1%以下、
Sn:0.0005%以上0.1%以下、
B:0.0005%以上0.01%以下、
Ca:0.001%以上0.01%以下、
REM:0.001%以上0.01%以下、
Co:0.05%以上5%以下、
Ni:0.05%以上5%以下および
Cu:0.2%以上4%以下
の1種または2種以上を含むことを特徴とする無方向性電磁鋼板。 In Claim 1 or 2, Furthermore, by mass% Sb: 0.0005% or more and 0.1% or less,
Sn: 0.0005% to 0.1%,
B: 0.0005% or more and 0.01% or less,
Ca: 0.001% to 0.01%,
REM: 0.001% to 0.01%,
Co: 0.05% or more and 5% or less,
A non-oriented electrical steel sheet comprising one or more of Ni: 0.05% to 5% and Cu: 0.2% to 4%. - 質量%で、
Si:5.0%以下、
Mn:2.0%以下、
Al:2.0%以下および
P:0.05%以下
を、下記式(1)を満足する範囲において含み、さらに
C:0.008%以上0.040%以下、
N:0.003%以下および
Ti:0.04%以下
を、下記式(2)を満足する範囲において含有する、鋼スラブを、1000~1200℃で均熱保持した後熱間圧延し、次いで1回または中間焼鈍を挟む2回以上の冷間圧延または温間圧延にて最終板厚とした後、仕上げ焼鈍を施すに当たり、前記仕上げ焼鈍に先立ち、800℃以上950℃以下の温度に30秒以上保持する熱処理を少なくとも1回は施し、その後、仕上げ焼鈍を700℃以上850℃以下で行うことを特徴とする無方向性電磁鋼板の製造方法。
記
300≦85[Si%]+16[Mn%]+40[Al%]+490[P%]≦430 …(1)
0.008≦Ti*<1.2[C%] …(2)
但し、Ti*=Ti-3.4[N%] % By mass
Si: 5.0% or less,
Mn: 2.0% or less,
Al: 2.0% or less and P: 0.05% or less are included within the range satisfying the following formula (1), and C: 0.008% or more and 0.040% or less,
A steel slab containing N: 0.003% or less and Ti: 0.04% or less in a range satisfying the following formula (2) is kept hot at 1000 to 1200 ° C. and then hot-rolled, and then once or in the middle Heat treatment is performed at a temperature of 800 ° C or higher and 950 ° C or lower for 30 seconds or more prior to the final annealing before the final annealing after the final thickness is obtained by cold rolling or warm rolling at least twice with annealing. Is applied at least once, and then finish annealing is performed at 700 ° C. or higher and 850 ° C. or lower.
300 ≦ 85 [Si%] + 16 [Mn%] + 40 [Al%] + 490 [P%] ≦ 430 (1)
0.008 ≦ Ti * <1.2 [C%] (2)
However, Ti * = Ti-3.4 [N%] - 請求項4において、Si、Mn、AlおよびPの含有量が、質量%で、
Si:3.5%超5.0%以下、
Mn:0.3%以下、
Al:0.1%以下および
P:0.05%以下
であることを特徴とする無方向性電磁鋼板の製造方法。 In Claim 4, content of Si, Mn, Al, and P is the mass%,
Si: more than 3.5% and less than 5.0%
Mn: 0.3% or less,
A method for producing a non-oriented electrical steel sheet, wherein Al: 0.1% or less and P: 0.05% or less. - 請求項4または5において、さらに、質量%で
Sb:0.0005%以上0.1%以下、
Sn:0.0005%以上0.1%以下、
B:0.0005%以上0.01%以下、
Ca:0.001%以上0.01%以下、
REM:0.001%以上0.01%以下、
Co:0.05%以上5%以下、
Ni:0.05%以上5%以下および
Cu:0.2%以上4%以下
の1種または2種以上を含むことを特徴とする無方向性電磁鋼板の製造方法。 In Claim 4 or 5, Furthermore, Sb: 0.0005% or more and 0.1% or less by mass%,
Sn: 0.0005% to 0.1%,
B: 0.0005% or more and 0.01% or less,
Ca: 0.001% to 0.01%,
REM: 0.001% to 0.01%,
Co: 0.05% or more and 5% or less,
A method for producing a non-oriented electrical steel sheet, comprising one or more of Ni: 0.05% to 5% and Cu: 0.2% to 4%.
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Also Published As
Publication number | Publication date |
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EP2679695A1 (en) | 2014-01-01 |
BR112013020657B1 (en) | 2019-07-09 |
CN103392021B (en) | 2014-10-29 |
EP2679695B1 (en) | 2016-05-18 |
KR20130087611A (en) | 2013-08-06 |
EP2679695A4 (en) | 2014-10-29 |
KR101412363B1 (en) | 2014-06-25 |
CA2822206A1 (en) | 2012-08-30 |
RU2536711C1 (en) | 2014-12-27 |
CA2822206C (en) | 2016-09-13 |
MX2013009670A (en) | 2013-10-28 |
BR112013020657A2 (en) | 2016-10-18 |
CN103392021A (en) | 2013-11-13 |
US20130306200A1 (en) | 2013-11-21 |
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