CN101310034B - Highly strong, non-oriented electrical steel sheet and method for manufacture thereof - Google Patents
Highly strong, non-oriented electrical steel sheet and method for manufacture thereof Download PDFInfo
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- CN101310034B CN101310034B CN2006800426737A CN200680042673A CN101310034B CN 101310034 B CN101310034 B CN 101310034B CN 2006800426737 A CN2006800426737 A CN 2006800426737A CN 200680042673 A CN200680042673 A CN 200680042673A CN 101310034 B CN101310034 B CN 101310034B
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2202/00—Physical properties
- C22C2202/02—Magnetic
Abstract
Disclosed is a non-oriented electrical steel sheet having a high strength, excellent magnetic properties and excellent productivity. The steel sheet comprises 0.010% by mass or less of C and 0.010% by mass or less of N, provided that C + N = 0.010% by mass, and also comprises 1.5 to 5.0% by mass of Si and 0.8% by mass or less of Ti or a mixture of Ti and V, provided that (Ti + V)/(C + N) = 16. The steel sheet may also have a content of a non-recrystallized recovery structure of 50% or more.
Description
Technical field
The present invention relates to highly strong, non-oriented electrical steel sheet (high-strength non-orientedelectrical steel sheet) and manufacture method thereof.Steel plate of the present invention be particularly suitable for being used in the rotor of quick peeler as typical case, be applied with on the electromagnetic component of big stress.Here as quick peeler, for example can enumerate servomotor of the CD-ROM drive motor of turbo-generator, electromobile and hybrid vehicle or robot, work mechanism etc.
Background technology
In recent years, the development of the drive system of Yin Mada can be carried out the frequency control of driving power, thus carry out variable-speed operation motor, increase with the motor that carries out high speed rotating more than the commercial frequency.In following the motor of this high speed rotating, the centrifugal force and the rotation radius that act on the rotor (rotor) are proportional, and become big with the square proportional of speed of rotation.Therefore, particularly the rotor material of big-and-middle-sized high-speed motor requires high strength (particularly advantages of higher tensile strength (tensile strength)).
And, that employing in the CD-ROM drive motor of hybrid vehicle, compressor motor etc. in recent years increases, imbed in the magnetite type DC conversion control motor (inverter controlled brushlessDC motor), on rotor, slit is set and buries magnetite underground.Therefore, when motor rotates stress concentration in the narrow cross-over connection portion between the slit, thereby the core material that in rotor, the uses physical strength (mechanical strength) of having relatively high expectations.And owing to acceleration and deceleration running, the vibration of stressed condition along with motor changes, thereby the magnetic core that uses in rotor (iron core) material preferably has higher fatigue strength.
On the other hand, rotary machine such as motor, generator, owing to utilize electromagnetic phenomenon, thereby the former material of its magnetic core also requires electromagnetic property (electromagnetical properties) good (being iron loss (iron loss)) lower, and preferably magneticflux-density (magnetic flus density) is also higher.
Particularly, in the high speed rotating motor, because the eddy current that is produced by the high frequency magnetic flux becomes the reason that moyor (mortor efficiency) reduces, thereby high frequency iron loss low (being the high frequency iron loss characteristic good) importantly.
Usually, rotor uses the non-oriented electromagnetic steel sheet having carry out after the punching press perforation with the magnetic core lamination, but can not satisfy under the situation of above-mentioned physical strength at the former material of high speed rotating motor rotor, has to use more high-strength cast steel system rotor etc.But, because foundry goods system rotor is one thing but not layered product, thereby the problem that exists so-called eddy current damage (eddy current loss) to rise significantly than the rotor of lamination electro-magnetic steel plate.
Therefore, require excellent in magnetic characteristics and high-intensity electro-magnetic steel plate as the former material of rotor.
High strength method as steel plate, known have solution strengthening (solid solutionhardening), precipitation strength (precipitation hardening), crystalline particle miniaturization to strengthen (fine-grain hardening) and complex tissue reinforcement (complex-phase hardening) etc., because these enhancement methods all make the magnetic properties variation, thus generally extremely difficulty have intensity and magnetic properties simultaneously.
Under this situation,, some technology have been proposed for having high-intensity non-oriented electromagnetic steel sheet having.
For example, in Japanese kokai publication sho 60-238421 communique following method being disclosed: makes Si content be increased to 3.5～7.0% (quality %, below identical), and add element such as Ti, W, Mo, Mn, Ni, Co, Al for solution strengthening and realize high strength.And, following method is disclosed except above-mentioned enhancement method in Japanese kokai publication sho 62-112723 communique: by control final annealing (final annealing) condition, make the crystallization particle diameter at 0.01～5.0mm, thereby improve magnetic properties.
But, aforesaid method is being applied to be easy to generate problems such as steel plate fracture in the rolling line after hot rolling under the situation of plant produced, exist yield rate to reduce, have to stop the problem of production line etc.In addition, for steel plate fracture, be that hundreds of ℃ warm-rolling (warm rolling) then can reduce with the cold rolling steel billet temperature that is made as.But, need be used for the equipment reply of warm-rolling, the restriction change in the production is big etc., increases the burden on the process management.
And, the method for implementing solution strengthening in the steel of Si content 2.0～3.5% by Mn and Ni is disclosed in Japanese kokai publication hei 2-22442 communique.And, in Japanese kokai publication hei 6-330255 communique, disclose at Si content more than 2.0, in the steel of less than 4.0, utilize precipitation strength and grain refined hardened technology based on the carbonitride (carbonitride) of Nb, Zr, Ti and V; And disclose the solution strengthening that additional on this basis Mn of interpolation and Ni cause in the Japanese kokai publication hei 2-8346 communique, realized the technology of high strength and magnetic properties simultaneously.
But, in the method for Japanese kokai publication hei 2-22442 communique record, can not obtain full intensity, in the method for Japanese kokai publication hei 6-330255 communique and Japanese kokai publication hei 2-8346 communique, obtain under the high-intensity situation, leave so-called magnetic properties and reduce bigger technical task.
And for the steel plate of producing by aforesaid method, even learn the fatigue characteristic that when estimating fatigue characteristic, obtain to obtain meeting under the high-intensity situation expectation.That is, only improve endurance (yield strength), the tensile strength of steel, the situation that can not improve fatigue characteristic is more, does not also establish the material method of design of considering fatigue characteristic, present situation that Here it is.
As the high-strength magnetic steel sheet that is conceived to fatigue characteristic, following technology is disclosed in TOHKEMY 2001-234303 communique: for Si content at the electro-magnetic steel plate below 3.3%, by forming the crystallization control particle diameter, reach the above safe range of stress of 350MPa according to its steel.But in the method, the arrival rank of safe range of stress itself lower (actual achievement be approximately maximum 430MPa) can not satisfy the rank of recent requirement, and for example safe range of stress (fatigue limit) is more than the 500MPa.
Manufacture method as high-strength magnetic steel sheet, following technology is disclosed in this external TOHKEMY 2005-113185 communique: with respect to the steel that contains 0.2～3.5% Si, by implementing high strength at the inner residual process tissues of steel (work hardening structure).As its concrete grammar following method being disclosed: does not heat-treat after cold rolling, even or heat-treat also not arrive and be equivalent to more than 750 ℃, keep the degree more than 30 seconds, preferably be made as below 700 ℃, so preferred below 650 ℃, below 600 ℃, below 550 ℃ and below 500 ℃.Wherein, as actual achievement and illustration makes the worked structure rate with 750 ℃ of annealing of-30 seconds is 5%, be 20% in-30 seconds, be 50% in-30 seconds with 600 ℃ with 700 ℃.
In this case, because annealing temperature is a low temperature, thereby there is the so-called problem that can not carry out the shape correction of sufficient rolled band steel.If the steel plate shape defect, then produce lamination process become motor with the dutycycle (lamination factor) behind the magnetic core etc. reduce, problem such as stress distribution when rotating as rotor high-speed is inhomogeneous.
And general custom is that the final annealing of non-oriented electromagnetic steel sheet having utilizes continuous annealing furnace to carry out, and is adjusted into the atmosphere that contains the hydrogen more than several % for the oxidation that suppresses surface of steel plate in the stove.In this continuous annealing apparatus, implement as when being lower than 700 ℃ low-temperature annealing, being not only the switching that furnace temperature sets needs the time, also needs to replace furnace atmosphere in order to prevent the hydrogen outburst, produces more operational restriction.
And, after high temperature final annealing, coating coating-sintering processes etc., for example import worked structure and use under the situation of this technology by the system of rerolling, append manufacturing process, cost rises, the restriction on the generation equipment.And, also produce the insulating coating of coating, agglomerating surface of steel plate behind the final annealing, destroyed and problem that insulativity reduces in processing treatment thereafter.
And disclose following technology in Japanese kokai publication hei 4-337050 communique: the cold rolling back steel plate that to Si is 4.0～7.0% composition is to heat-treat with the specified temp that concerns defined of Si content, the recrystallize rate that makes crystal structure is below 95%, and surplus is actually rolling structure and realizes strengthening.In the formula, for example with under 700 ℃ of situations of heat-treating, need about Si more than 5.9%.In this technology, can obtain having concurrently 80kgf/mm
2The soft magnetic material of the practicality of above high-tensile, unit elongation to a certain degree and good magnetic properties.
And following method being disclosed in TOHKEMY 2005-264315 communique: is containing Si:0.2～4.0%, in the electro-magnetic steel plate of ferritic phase as principal phase, add Ti, Nb, Ni etc. steel inner produce diameter below 0.050 μ m intermetallic compound and realize strengthening.In this technology, can not damage cold-rolling property etc. and produce and have 60kgf/mm
2Above tensile strength and wear resistant, magneticflux-density, the non-oriented electromagnetic steel sheet having that has excellent core loss.
As mentioned above, though disclose some technology for high-intensity non-oriented electromagnetic steel sheet having, but present situation is to guarantee necessary strength and good magnetic properties and steel plate shape, can not utilize common electrical magnetic steel plate producing apparatus stably to make industrial.
Summary of the invention
The object of the present invention is to provide a kind of non-oriented electromagnetic steel sheet having and manufacture method thereof, in the manufacturing of common non-oriented electromagnetic steel sheet having, in fact do not append restriction or new process that steel plate is made, and high strength and steel plate shape and magnetic properties are all good.
Another object of the present invention is to, with high strength and have the good non-oriented electromagnetic steel sheet having of good magnetic properties and fatigue characteristic and manufacturing and propose with its favourable manufacture method.
Main idea of the present invention is as described below:
(1) a kind of highly strong, non-oriented electrical steel sheet, it is characterized in that, having following compositions forms: in quality %, C and N are suppressed for below the C:0.010% and below the N:0.010% and C+N≤0.010%, contain Si:1.5% above, 5.0% below, Mn:3.0% is following, Al:3.0% is following, below the P:0.2%, below the S:0.01%, and contain more than the Ti:0.05% in the scope that satisfies Ti/ (C+N) 〉=16, below 0.8%, surplus is Fe and unavoidable impurities; And the non-recrystallization recovery organization in the steel plate (non-rerystallized, count more than 50% with area occupation ratio by the ratio that exists recoverystructure).
Here, describe for recrystallize and non-recrystallization recovery organization.At first, recrystallize be meant form again that defect concentration is lower, stable crystalline particle on the thermodynamics, the phenomenon of growing up in the time of the higher matrix of the defect concentration around nibbling.Defect concentration sharply reduces because crystal boundary moves in recrystallize.
On the other hand, recover to be meant that defective itself moves and the dislocation desity reduction towards depression (sink) heat not according to passing through of crystal boundary, the phenomenon of strain energy reduction as a result.In the continuous annealing of the short period of time of recovering as in non-oriented electromagnetic steel sheet having, being suitable for usually, under the situation that the condition more than 500 ℃ is handled, clearly occur in annealing temperature.Exist though recovery organization and recrystallized structure are mixed, the annealing recrystallization under the high temperature is got over the tool advantage.In the electro-magnetic steel plate of common composition, sharply carry out at recrystallize more than 600～650 ℃, become recrystallized structure in major part more than 700 ℃.
In addition, carrying out in the annealed steel recovery organization of recrystallized structure and non-recrystallization, tissue that can be by carrying out (microtexture: microstructure) observe and distinguish easily more than 500 ℃ with opticmicroscope.Here, structure observation can followingly carry out usually: thickness of slab direction cross section is ground the back, carried out etching with nital (nitric alcohol solution) etc.
Wherein, in the invention of above-mentioned (1),, be preferably more than the Si:1.5%, below 4.0% in quality %.And, in the invention of above-mentioned (1), in quality %, preferred and then contain at least a kind that is selected from Ni:0.1～5.0%, Sb:0.002～0.1%, Sn:0.002～0.1%, B:0.001～0.01%, Ca:0.001～0.01%, Rem:0.001～0.01% and Co:0.2～5.0%.These preferred conditions also can independent assortment.
(2) a kind of manufacture method of highly strong, non-oriented electrical steel sheet, it is characterized in that, plate slab with following compositions composition is carried out hot rolling: in quality %, C and N are suppressed for below the C:0.010% and below the N:0.010% and C+N≤0.010%, contain Si:1.5% above, 5.0% below, Mn:3.0% is following, Al:3.0% is following, below the P:0.2 quality %, below the S:0.01 quality %, and contain more than the Ti:0.05 quality % in the scope that satisfies Ti/ (C+N) 〉=16, below the 0.8 quality %; Then, form the cold rolling coiled material of final thickness of slab by cold rolling or warm-rolling after, when carrying out final annealing, with this final annealing in annealing temperature be more than 700 ℃, below 850 ℃, stove internal tension (strip unit tension in furnace) is for to carry out more than the 2.5MPa, below the 20MPa.
Here, the stove internal tension is the tension force on the unit cross-sectional area of steel band of the steel band stove section part (being mostly heating zone (heating section) back segment or soaking zone (soaking section)) that is in top temperature in annealing furnace.
In addition, in the invention of above-mentioned (2), with the invention of above-mentioned (1) in the same manner, preferably surplus is Fe and unavoidable impurities in the one-tenth of plate slab is grouped into.
And, in the invention of above-mentioned (2), with the invention of above-mentioned (1) in the same manner, preferably contain more than the Si:1.5%, below 4.0%, and/or contain at least a kind that is selected from Ni:0.1～5.0%, Sb:0.002～0.1%, Sn:0.002～0.1%, B:0.001～0.01%, Ca:0.001～0.01%, Rem:0.001～0.01% and Co:0.2～5.0% in quality % in quality %.
The invention of above-mentioned (2) is specially adapted to obtain the steel plate of the invention of above-mentioned (1), and promptly the ratio that exists of non-recrystallization recovery organization is counted steel plate more than 50% with area occupation ratio.
And the inventor etc. for the manufacturing and the influence that relates to the various enhancement methods of mechanical characteristics, fatigue characteristic and magnetic properties to non-oriented electromagnetic steel sheet having, have carried out research with keen determination in order to solve above-mentioned problem.For solution strengthening, the influence to the manufacturing (bending (bending) characteristic and the cold-rolling property of hot-rolled steel sheet and hot-roll annealing steel plate specifically) of the high alloy electro-magnetic steel plate of the addition that improved solution strengthening elements such as Si studies in great detail for alloying constituent.
Its result, find as follows about the carbonitride forming element:
(a) by reduce solid solution C, N as far as possible, even, also can increase substantially its rolling property for as containing the high quality steel of the Si that surpasses 3.5 quality %.
(b) for this reason, effectively, reduce C, N amount, and with respect to C, N with the abundant carbonitride forming elements such as Ti, V, Nb, Zr that add of atomic ratio measuring superfluously.
According to above-mentioned opinion, when making the high alloy electro-magnetic steel plate, can realize reducing significantly the high productivityization of the problem on the operation such as steel plate fracture.
Then, the influence of mechanical characteristics, fatigue characteristic and the magnetic properties generation of electro-magnetic steel plate is investigated, is found as follows for above-mentioned carbonitride forming element:
(c) carbonitride of Ti, V, Nb, Zr, effective to high-tensileization by the precipitation strength effect, on the other hand, its amount causes the deterioration of fatigue characteristic, magnetic properties (iron loss and magneticflux-density) for a long time.
(d) with respect to this, Ti, V, Nb, Zr with respect to C, N add superfluously have the solution strengthening effect, improve fatigue characteristic when increasing substantially tensile strength, and the deterioration of magnetic properties is also compared minimizing significantly with the situation of precipitation strength.
And, the result for main solid solution element is investigated the influence of mechanical characteristics, fatigue characteristic and magnetic properties generation, find as follows:
(e) from realizing the viewpoint of mechanical characteristics and magnetic properties simultaneously, the most effectively, utilize the solution strengthening of Si in the principal element that in non-oriented electromagnetic steel sheet having, adds.But when the Si addition was superfluous, though improve tensile strength (tensile strength), fatigue characteristic are deterioration significantly.That is, balance to improve mechanical characteristics, fatigue characteristic and magnetic properties well, there is optimum range in the Si addition.
The present invention develops according to above neodoxy, and its main composition is as follows:
(3)
(3-1) highly strong, non-oriented electrical steel sheet of good and fatigue characteristic and excellent in magnetic characteristics of a kind of manufacturing, it is characterized in that, has following composition: in quality %, making C and N is that C:0.010% is following with below the N:0.010%, and C+N≤0.010%, contain Si: greater than 3.5% and below 5.0%, below the Mn:3.0%, below the Al:3.0%, below the P:0.2%, and below the S:0.01%, or also contain below the Ni:5.0%, and the scope in satisfied (Ti+V)/(C+N) 〉=16 contains and adds up to more than 0.01%, Ti below 0.8%, among the V any a kind or 2 kinds, surplus is Fe and unavoidable impurities.
(3-2) highly strong, non-oriented electrical steel sheet of good and fatigue characteristic and excellent in magnetic characteristics of a kind of manufacturing, it is characterized in that, has following composition: in quality %, making C and N is that C:0.010% is following with below the N:0.010%, and C+N≤0.010%, contain Si: greater than 3.5% and below 5.0%, below the Mn:3.0%, below the Al:3.0%, below the P:0.2%, and below the S:0.01%, or also contain below the Ni:5.0%, and the scope in satisfied (Nb+Zr)/(C+N) 〉=10 contains and adds up to more than 0.01%, Nb below 0.5%, among the Zr any a kind or 2 kinds, surplus is Fe and unavoidable impurities.
(3-3) highly strong, non-oriented electrical steel sheet of good and fatigue characteristic and excellent in magnetic characteristics of a kind of manufacturing, it is characterized in that, has following composition: in quality %, making C and N is that C:0.010% is following with below the N:0.010%, and C+N≤0.010%, contain Si: greater than 3.5% and below 5.0%, below the Mn:3.0%, below the Al:3.0%, below the P:0.2%, and below the S:0.01%, or also contain below the Ni:5.0%, and satisfy 0.01%≤(Ti+V+Nb+Zr)≤0.5% and (Ti+V+Nb+Zr)/(C+N) 〉=16 scope contain Ti, at least a kind and Nb among the V, among the Zr at least a kind, surplus is Fe and unavoidable impurities.
(3-4) highly strong, non-oriented electrical steel sheet of good and fatigue characteristic and excellent in magnetic characteristics of a kind of manufacturing, in each described invention in above-mentioned (3-1) to (3-3), it is characterized in that, also contain be selected from Sb:0.002～0.1%, Sn:0.002～0.1%, B:0.001～0.01%, Ca:0.001～0.01%, Rem:0.001～0.01% and Co:0.2～5.0% more than a kind or 2 kinds.
(4) manufacture method of the highly strong, non-oriented electrical steel sheet of good and fatigue characteristic and excellent in magnetic characteristics of a kind of manufacturing, it is characterized in that, after carrying out hot rolling in the plate slab of forming shown in each invention in above-mentioned (3-1) to (3-4), implement hot-rolled sheet annealing as required, then, forming final thickness of slab by once cold rolling or warm-rolling or the cold rolling or warm-rolling more than the secondary of process annealing, is that condition more than 700 ℃, below 1050 ℃ is carried out final annealing with annealing temperature then.
Here, above-mentioned final thickness of slab is preferably more than 0.15mm.
According to the present invention, the invention of particularly above-mentioned (1) and (2) is formed and tissue by predetermined component, does not append restriction that steel plate makes or new operation, and high strength and steel plate shape and all good non-oriented electromagnetic steel sheet having of magnetic properties just can be provided.
And according to the present invention, the invention of particularly (3) ((3-1)～(3-4)) and (4) can stably obtain not only high strength and have good magnetic properties, and material of excellent fatigue characteristics, and the also good non-oriented electromagnetic steel sheet having of manufacturing.
Description of drawings
Unit=quality %) and annealing temperature (longitudinal axis: unit=℃) and the recrystallize rate (numeral that circle is interior: the figure of relation unit=area %) Fig. 1 is an expression Ti amount (transverse axis:.
Fig. 2 is (C+N) amount (transverse axis: unit=quality %) to (longitudinal axis: the chart of the influence of Chan Shenging unit=number of times) of the steel plate trafficability characteristic (number of bends) in the manufacturing line in the expression steel.
Fig. 3 is the (transverse axis: unit=quality %) to cold-rolling property (degree of depth is split on the limit of rolled sheet material the end face) (longitudinal axis: the chart of the influence that unit=mm) produces of (C+N) amount in the expression steel.
Fig. 4 is with Ti amount (transverse axis: unit=quality %) to (longitudinal axis: the influence of Chan Shenging unit=number of times), the chart that (C+N) scale shows in the steel for 4 levels of the steel plate trafficability characteristic (number of bends) in the manufacturing line in the steel.
Fig. 5 be with Ti/ (C+N) than (transverse axis) to (longitudinal axis: the influence of Chan Shenging unit=number of times), the chart that shows for (C+N) scale in 4 grades of steel of the steel plate trafficability characteristic (number of bends) in the manufacturing line.
Fig. 6 is with (the transverse axis: unit=quality %) to cold-rolling property (degree of depth is split on the limit of rolled sheet material the end face) (longitudinal axis: the influence of unit=mm) produce, the chart that shows for (C+N) scale in 4 grades of steel of Ti amount in the steel.
Fig. 7 be with Ti/ (C+N) than (transverse axis) to cold-rolling property (degree of depth is split on the limit of rolled sheet material the end face) (longitudinal axis: the influence that unit=mm) produces, the chart that shows for (C+N) scale in 4 grades of steel.
Fig. 8 is with (the transverse axis: unit=quality %) to tensile strength (the TS) (longitudinal axis: the influence of unit=MPa) produce, the chart that shows for (C+N) scale in 4 grades of steel of Ti amount in the steel.
Fig. 9 is with (the transverse axis: unit=quality %) to safe range of stress (the FS) (longitudinal axis: the influence of unit=MPa) produce, the chart that shows for (C+N) scale in 4 grades of steel of Ti amount in the steel.
Figure 10 is with Ti amount (transverse axis: unit=quality %) to high frequency iron loss (W
10/1000) (longitudinal axis: unit=W/kg) produces the influence in the steel, the chart that shows for (C+N) scale in 4 grades of steel.
Wherein, in Fig. 4 to Figure 10, ◆ expression C+N:0.0038～0.0048 quality %; ■ represents C+N:0.0074～0.0092 quality %; ▲ expression C+N:0.0175～0.0196 quality %; * expression C+N:0.0353～0.0391 quality %.
Embodiment
Below, " % " expression relevant with composition just means quality % when not particularly pointing out.
(inventive principle)
At first, the inventive principle to above-mentioned (1) and (2) describes.
Contrivers etc. have studied with keen determination and have been used for industrial stable and realize method as the non-oriented electromagnetic steel sheet having of the high strength of one of above-mentioned problem and magnetic properties simultaneously with good steel plate shape manufacturing.In the high strength of this requirement, be specially tensile strength more than 600MPa, preferably more than 700MPa, and then preferably more than 800MPa.And desired magnetic properties, particularly high frequency are hanged down iron loss characteristic, are W in the non-oriented electromagnetic steel sheet having of 0.35mm at thickness of slab for example
10/400Value is preferably below the 40W/kg for below the 50W/kg, and then is preferably the following level of 30W/kg.
The result of above-mentioned research finds particularly surpassing in the High Strength Steel of 700MPa as tensile strength, effectively steel plate is organized in inhibition recrystallize in the final annealing and gives over to recovery organization.But,, must carry out at the low temperature below 600 ℃ in the final annealing temperature for the former material of non-oriented magnetic steel that utilizes ordinary steel the to form tissue that is restored.In order to utilize this low-temperature annealing to come stably to make, must solve the displacement of steel plate shape variation, annealing atmosphere, the change of furnace temperature condition expends problems such as very big time and working load industrial.
When carrying out relevant with composition of steel various research, discovery is by forming steel and form with respect to the abundant Ti that adds of C and N superfluously, even also can stably obtain the effective recovery organization of high strength with the final annealing temperature more than 700 ℃ identical with the annealing of common non-oriented electromagnetic steel sheet having.
(experiment 1)
That is, represent to study Ti addition and final annealing temperature (soaking time is 20s) change the influence that produces to the recrystallize of the 2.8%Si-0.35%Al steel that is reduced to C+N≤0.01% result at Fig. 1.Here, the transverse axis of chart is Ti amount (quality %), the longitudinal axis be annealing temperature (℃), the recrystallize rate (recrystallization ratio) (area %) under this condition of numeral in each circle.Wherein, the recrystallize rate also can be calculated by the optical texture observations in thickness of slab direction cross section, and the ratio of non-recrystallization recovery organization (area %) is 100-recrystallize rate (area %).
Usually, in non-oriented electromagnetic steel sheet having, Ti is the harmful element that makes the magnetic properties variation, usually be controlled at below the 0.005 quality %, owing in this Ti content rank, sharply carrying out recrystallize more than 650 ℃, thereby must carry out final annealing at the low temperature below 600 ℃ for the tissue that stably is restored.
On the other hand, when finding to add the Ti more than the 0.05 quality %, recrystallize begins temperature and rises more than 100 ℃ the tissue even the annealing temperature more than 700 ℃ of industrial enforcement in the past also can stably be restored.And find by making the final annealing temperature more than 700 ℃, below 850 ℃, more than the stove internal tension 2.5MPa, below the 20MPa, tissue can stably be restored, and can control the steel plate shape well, finish high strength, magnetic properties, steel plate shape, highly strong, non-oriented electrical steel sheet and manufacture method thereof that productivity is good.
Then, the inventive principle to above-mentioned (3) and (4) describes.
Below, the experimental result as basis of the present invention is described.
(experiment 2)
At first, for investigate steel form to as Si content surpass the influence of the manufacturing generation of 3.5% high quality steel, utilization can be made cold crucible (cold crucible inductionmelting furnace) the vacuum high frequency melting furnace of ultra-high purity steel, melts out the Si amount to be controlled at 4.1～4.3% scope and to make C, N amount that the test steel ingot of various variations take place.Then, to resulting steel ingot, be hot-rolled down to thickness of slab 2mm after, implement annealing (hot-rolled sheet annealing) with 900 ℃ after, be cold-rolled to thickness of slab 0.35mm.
At this moment, the hot-roll annealing plate being cut out with the 30mm width, is that 30 ℃ of enforcement bending radius are that 15mm, angle of bend are 90 ° repeated flex test with temperature, and the steel plate trafficability characteristic on the manufacturing line is carried out Simulation evaluation.Wherein, under the situation of the material of this repeated flex number of times less than 10 times, the fracture frequency on the manufacturing line increases as can be known.And as the evaluation of cold-rolling property, the degree of depth (edge crack length) is split on the limit of having measured the end face of above-mentioned hot-roll annealing plate.
Its result as shown in Figures 2 and 3.Here, the transverse axis of chart is (C+N) amount (quality %) in the steel, the longitudinal axis be respectively steel plate trafficability characteristic (number of bends) in the manufacturing line and cold-rolling property (degree of depth is split on the limit of rolled sheet material end face) (mm).
As shown in Figures 2 and 3, steel plate trafficability characteristic (curved characteristic of hot-rolled steel sheet) in the manufacturing line and cold-rolling property (degree of depth is split on the limit) and manufacturing depend on the total amount of C and N strongly as can be known.That is, C+N amounted to be reduced to 0.0015% when following, even the high quality steel of 4.2%Si grade also shows sufficient manufacturing, but the rapid variation of manufacturing during the increase of C+N amount.
But in the prior art of utilizing general device such as converter refining, degassing secondary refining, it is very difficult that the C+N amount is stabilized in below 0.0015%.
(experiment 3)
Consider whether the solid solution C, the N that exist in the steel are the major cause of the manufacturing reduction of evaluation this time, attempt adding carbonitride and produce element and separate out fixation of C, N.
Promptly, utilize the electric furnace manufacturing Si amount to be controlled at 4.1～4.3% scope, with the overall control of C+N is 4 levels of (1) 0.0038～0.0048% scope, (2) 0.0074～0.0092% scope, (3) 0.0175～0.0196% scope, (4) 0.0353～0.0391% scope, and makes the Ti addition that the steel ingot of various variations take place.Then, be hot-rolled down to thickness of slab 2mm, after the annealing of 900 ℃ of enforcement hot-rolled sheets, be cold-rolled to thickness of slab 0.35mm, implement final annealings with 950 ℃.
With respect to the sample that obtains like this, will with above-mentioned situation under in the same manner, the result who investigates for the steel plate trafficability characteristic on the manufacturing line (curved characteristic of hot-rolled steel sheet) and cold-rolling property (degree of depth is split on the limit) is illustrated respectively in Fig. 4 to Fig. 7.Here, the transverse axis of Fig. 4 and Fig. 6 is a Ti amount (quality %) in the steel, the transverse axis of Fig. 5 and Fig. 7 be in the steel Ti amount (quality %) with respect to the C+N amount (in the steel in C amount and the steel N measure sum: ratio quality %), i.e. Ti/ (C+N).And the longitudinal axis of Fig. 4 and Fig. 5 is the steel plate trafficability characteristic (number of bends) in the manufacturing line, the longitudinal axis of Fig. 6 and Fig. 7 be cold-rolling property (degree of depth is split on the limit of rolled sheet material end face) (mm).And, in the drawings, black rhombus ◆ the above-mentioned level (1) of expression C+N; Black four jiaos of ■ represent above-mentioned level (2); Black triangle ▲ represent above-mentioned level (3); Cross mark * represent above-mentioned level (4).
Learn by The above results, by measuring with the about Ti that adds more than 4 times of atomic ratio (is more than 16 times with quality % ratio) superfluously with respect to C+N, the curved characteristic and the cold-rolling property of hot-rolled steel sheet are greatly improved, even can also can stably make high quality steel in the C+N of industrial mass-produced purity grade amount.
But if C+N amount is too many, then Ti adds the manufacturing that causes and improves effect and diminish, and hot-rolled steel sheet number of bends and cold rolling limit are split the degree of depth and all reached debatable rank on the industrial production (number of bends: the degree of depth is split on less than 10 times, limit: surpass 3mm).
And learn that even to improve the C+N magnitude of manufacturing fully other by adding Ti, the Ti addition surpasses also variation of 0.8% o'clock manufacturing.And, in the steel of the higher and composition that the Ti addition is less of C+N amount and the steel of Ti addition surplus, find that limit when cold rolling is split to reach more than the 10mm, can also see the steel plate that produces fracture.
(experiment 4)
Then, utilize from the resulting steel plate test film that cut out parallel investigation mechanical characteristics and fatigue characteristic with rolling direction.Here, mechanical characteristics is utilized No. 5 tension test sheets of JIS (parallel portion length is 25mm), estimates with the tensile strength in the tension test.And fatigue characteristic are utilized the fatigue test piece of parallel portion length for 15mm, use stress ratio: part stretching (stretching-stretching) fatigue test of 0.1, frequency: 20Hz is investigated, even will be through 10,000,000 (10
7) maximum stress that also can not produce the steel plate fracture after the circulation obtains as safe range of stress.
Resulting result such as Fig. 8 and shown in Figure 9.Here, the transverse axis of chart is a Ti amount (quality %) in the steel, the longitudinal axis of Fig. 8 be tensile strength (TS) (MPa), the longitudinal axis of Fig. 9 is safe range of stress (MPa).Wherein, the mark of being described is identical with relation and Fig. 4 to Fig. 7 of the level of C+N amount.
As shown in Figure 8, tensile strength TS and Ti addition all rise, and its effect is apparent more when C+N amount is high more.Think that its reason is the high steel of C+N amount, the carbonitride of Ti is separated out the high strength that the precipitation strength that causes causes and is advanced.On the other hand, infer that the high strength that solid solution Ti causes changes into main body in C+N amount lower steel and the steel of Ti addition with respect to the abundant surplus of C+N amount.
And, as shown in Figure 9, safe range of stress, opposite with the result of tensile strength when comparing with identical Ti addition rank, the lower group of C+N amount is represented higher fatigue characteristic.Infer that its reason is in the higher group of C+N amount, become big because the carbonitride size of separating out is easy, and its amount is more, thereby becomes the starting point of fatigure failure.
And, will utilizing the magnetic-measurement test film that cuts out equal amts from rolling direction and rolling right angle orientation, the result by Epstein method evaluation magnetic properties is shown in Figure 10.Here, the transverse axis of chart is a Ti amount (quality %) in the steel, and the longitudinal axis is high frequency iron loss (W
10/1000) (W/kg), the mark of C+N level is identical with Fig. 4 to Fig. 9.
As shown in the drawing, C+N measures higher group because of adding the rapid variation of a spot of Ti iron loss characteristic, and with respect to this, in the group that suppresses the C+N amount, it is slight that Ti adds the iron loss variation situation that causes.
Learn by above result of study, in order to obtain satisfying the non-oriented electromagnetic steel sheet having of the high strength considered industrial fully good manufacturing, the fatigue strength requirement opposite like this with good magnetic properties in higher aspect, importantly, in industrial possible scope, reduce in the high quality steel of C+N amount as far as possible, Ti as the element of separating out fixation of C, N, and is effectively utilized as the solution strengthening element.
According to above-mentioned opinion, so that the C+N amount is reduced to industrial permissible rank, an amount of add steel with an amount of carbonitride forming element (V, Nb, Zr) headed by the Ti as the basis, carry out system evaluation for the influence of adding alloying elements such as Si, Mn, Al, Ni, P, the clear steel of the best of learning is formed condition.
(steel composition)
Below, the qualification reason according to the definite composition compositing range of the present invention of above-mentioned opinion is described.
C:0.010% is following and N:0.010% is following and C+N≤0.010%
In the present invention, C and N are the harmful elements that significantly reduces the manufacturing of steel when existing with solid solution condition, but the carbonitride forming elements such as (inventing in (3), (4)) Nb, V, Zr by adding Ti in right amount or hereinafter describing can be reduced to the detrimentally affect to manufacturing the rank that can not become obstacle on the industrial-scale production.Because the generation of carbonitride also causes the magnetic properties deterioration, and then causes the deterioration of fatigue characteristic, thereby preferably reduces C and N within the bounds of possibility as far as possible.Therefore, suppress for below the C:0.010%, below the N:0.010% and C+N≤0.010%.
It is following and N:0.005% following and then it is following and below the N:0.003% to be preferably C:0.003% to be preferably C:0.005%.Though needn't contain C, N, the industrial lower limit that as far as possible reduces is respectively about 0.0001%.
Below the Si:1.5%, below 5.0%:
Si is except as reductor and usually using, and still improves the resistance of steel and has the principal element of the formation non-oriented electromagnetic steel sheet having of the effect that reduces iron loss.And, have higher solution strengthening ability.Promptly, owing to be to compare with other solution strengthening elements such as the Mn that in non-oriented electromagnetic steel sheet having, adds, Al and Ni, be balance to realize the element of high-tensileization, high-fatigue strengthization and low iron lossization well simultaneously, thereby in the present invention (1), (2), add more than 1.5%.And then preferably more than 2.0%.In the present invention (3), (4) and then add energetically more than 3.5%, the high characterization that effectively utilizes the reduction of the rising of the tensile strength that obtains along with the increase of Si amount, safe range of stress intensity and iron loss to bring.
On the other hand, increase though Si amount surpasses 5.0% o'clock tensile strength, safe range of stress intensity sharply reduces, and cracks manufacturing more reduce more in cold rolling.Think that its reason is to follow high Siization and the generation rule phase.And the Si amount surpasses 3.0% o'clock toughness and begins to reduce, and surpasses at 4.0% o'clock and clearly manifests the toughness deterioration.And surpass 5.0% o'clock toughness deterioration and become significantly, steel plate by and need highly control when rolling, productivity also reduces.Thus, establish Si amount on be limited to 5.0%.Preferably below 4.0%.In invention (1), (2), pay attention under the flexible situation, and then preferably below 3.5%.
Ti:0.05% is above, 0.8% below and Ti/ (C+N) 〉=16 (inventing (1), (2))
Following arbitrary condition (invention (3), (4))
(3-1) Ti+V:0.01% above, below 0.8% and (Ti+V)/(C+N) 〉=16,
(3-2) Nb+Zr:0.01% above, below 0.5% and (Nb+Zr)/(C+N) 〉=10,
Or (3-3) 0.01%≤(Ti+V+Nb+Zr)≤0.5%,
And (Ti+V+Nb+Zr)/(C+N) 〉=16
Ti is important key element in the present invention.That is, Ti has the effect of the recrystallization temperature that improves steel, even the final annealing temperature that has steel plate is increased to more than 750 ℃, and effect that also can residual fully non-recrystallization tissue in the present invention (1), (2).And Ti plays a role as the solution strengthening element and helps high-tensileization.In order to play consistently above-mentioned effect, Ti is more than 0.05% and Ti/ (C+N) 〉=the 16th, and is necessary.On the other hand, Ti surpasses at 0.8% o'clock, is known as the folding defective of squamous owing to be easy to generate, and manufacturing and yield rate reduce, thereby the upper limit is set at 0.8%.
And Ti has the formation carbonitride, and solid solution C, the N that will exist in steel separates out fixing and improve the effect of the manufacturing of high quality steel.And, also play a role as the solution strengthening element, also help high-tensileization, high-fatigue strengthization effectively.Particularly in the present invention (3) who Si is effectively utilized to greatest extent solution strengthening above 3.5% interpolation, (4), effectively utilize above-mentioned effect.That is, contain more than 0.01%, below 0.8% with V as same carbonitride forming element/solution strengthening element, and (Ti+V)/(C+N) 〉=16.In order stably to separate out fixation of C, N midway from manufacturing process, the total amount Ti+V of Ti and V is minimum also will to contain 0.01%, and owing to need add, thereby containing in the scope that satisfies (Ti+V)/(C+N) 〉=16 in quality % ratio with respect to C, N superfluously.Be preferably Ti+V more than 0.05%.On the other hand, reduce because Ti+V surpasses 0.8% o'clock manufacturing, thereby the upper limit of Ti+V is determined 0.8%.
Nb and Zr and above-mentioned Ti, V have the formation carbonitride in the same manner, make the solid solution C, the N that exist in steel separate out fixing and improve the effect of the manufacturing of high quality steel.And, also play a role as the solution strengthening element, help high-tensileization, high-fatigue strengthization effectively.Therefore, in the present invention (3), (4), also can replace Ti, V and use these elements.In order stably to separate out fixation of C, N midway from manufacturing process, the total amount Nb+Zr of Nb and Zr is minimum also will to contain 0.01%, and owing to need add, thereby containing in the scope that satisfies (Nb+Zr)/(C+N) 〉=10 in quality % ratio with respect to C, N superfluously.On the other hand, reduce because Nb+Zr surpasses 0.5% o'clock manufacturing, thereby the upper limit of Nb+Zr is determined 0.5%.
As mentioned above, Ti and V and Nb and Zr are as the carbonitride forming element, and solution strengthening element and play same effect, thereby can also compoundly contain above-mentioned 4 kinds of elements.In this case, in order stably to separate out fixation of C, N midway from manufacturing process, the total amount Ti+V+Nb+Zr of Ti, V, Nb, Zr is minimum also will to contain 0.01%, and owing to need add, thereby need to satisfy (Ti+V+Nb+Zr)/(C+N) 〉=16 in quality % ratio with respect to C, N superfluously.But, reduce because Ti+V+Nb+Zr surpasses 0.5% o'clock manufacturing, thus establish Ti+V+Nb+Zr on be limited to 0.5%.
In addition, guarantee the non-recrystallization recovery organization and realize the effect of high strength and magnetic properties simultaneously that Ti is better than Nb, V, Zr, thereby must add Ti in the present invention (1), (2).
Below the Mn:3.0%
Mn, preferably adds more than 0.03% still to the hot short effective elements of improving except being that the intensity based on solution strengthening is improved effective elements.But because superfluous interpolation causes the deterioration of iron loss, thereby its addition is limited to below 3.0%.
Below the Al:3.0%
Al also has the resistance that improves steel and the effect that reduces iron loss except the effect that the reductor as brute force plays a role.And, the intensity based on solution strengthening is risen effectively.But,, thereby establish and be limited to 3.0% on it because superfluous interpolation causes the reduction of rolling property.And then preferably below 2.0%.Be preferably Si+Al≤4.0% main the utilization in the present invention (1) based on the reinforcement of non-recrystallization tissue, (2).
In addition, neither contain this Al.For example, also the interpolation of Al can be suppressed at below 0.005%.That is, for example also can reduce Al, reduce precipitates such as AlN on the other hand and reduce iron loss by the Si deoxidation.Wherein, following being limited to about 0.0001% of Al amount in the industrial diminishbb steel.
Below the P:0.2%
P, very effective even more a spot of interpolation also can obtain significantly solution strengthening ability to high strength, preferably add more than 0.005%.But superfluous interpolation is owing to causing the caused embrittlement of segregation to cause the reduction of grain-boundary crack, rolling property, thereby its addition is limited in below 0.2%, and is preferred below 0.20%.Wherein, following being limited to about 0.001% of P amount in the industrial diminishbb steel.
Below the S:0.01%
Form the MnS sulfides superfluously when S exists, magnetic properties is reduced.And MnS also may become the starting point of fatigure failure.Therefore, the S amount is preferred in the steel reduces as far as possible, allows and contains to 0.01%, thereby establish its addition below 0.01%.Wherein, following being limited to about 0.0003% of S amount in the industrial diminishbb steel.
Other
The essentially consist of non-oriented electromagnetic steel sheet having of the present invention except mentioned component, also can separately or be known as magnetic properties with the complex method interpolation and improve the Ni of element, Sb, Sn, B, Ca, rare earth element (Rem) and Co as mentioned above.But its addition must be for not hindering the degree of purpose of the present invention.Be following ranges specifically.Sb:0.002～0.1%, Sn:0.002～0.1%, B:0.001～0.01%, Ca:0.001～0.01%, Rem:0.001～0.01%, Co:0.2～5.0% and below the Ni:5.0% are preferably 0.1～5.0%.
Particularly preferably be and add Ni.Promptly, the a lot of elements that help solution strengthening and high resistanceization, cause the reduction of saturation magnetic flux density by its interpolation, with respect to this, Ni can not reduce saturation magnetic flux density just can realize the very effective element that rises and reduce based on the iron loss of high resistanceization based on the intensity of solution strengthening.But Ni is expensive element, and superfluous interpolation causes cost very high, thereby preferably contains below 5.0%.
In addition, the surplus of establishing steel consists of Fe and unavoidable impurities.As unavoidable impurities, except the above-mentioned element of enumerating (former thereby situation about containing inevitably), can also enumerate Cu (use at raw material under the situation of scrap metal steel and may sneak into) etc. because of cost etc.
(structure of steel)
Then, the qualification reason to the steel plate tissue in the present invention (1), (2) describes.
In order to realize high strength and the magnetic properties as the object of the invention simultaneously, the steel plate tissue is preferably recovery organization.In the worked structure of rolling state, the remarkable variation of magnetic properties.On the other hand, when carrying out recrystallize by final annealing, though magnetic properties becomes well, the reduction of intensity is bigger.With respect to this, recovery organization forms by about annealing more than 500 ℃, and this recovery organization has higher intensity, and can obtain better magnetic properties.In the present invention (1), (2), importantly effectively utilize this recovery organization, in order to realize intensity and magnetic properties simultaneously, importantly, the recovery organization of this non-recrystallization has more than 50% in area occupation ratio in the thick section of steel plate is observed.
In addition and since in the present invention (3), (4) with solution strengthening as main reinforcement means, thereby needn't guarantee the non-recrystallization recovery organization.Therefore, as long as can guarantee intensity, also can establish recrystallized structure is 100%, guarantees more stable industrial productivity.But, be not to get rid of to use of the help of non-recrystallization recovery organization simultaneously to strengthening.
(manufacture method)
At last, manufacture method of the present invention is described, describe it and limit reason.
In the present invention, from the manufacturing process of steel melting till cold rolling, can implement according to the method that in general non-oriented electromagnetic steel sheet having, adopts usually.Particularly, the present invention is owing to measure the interpolation of control and carbonitride forming element by suitable C, N, even can debatablely surpass in the steel plate trafficability characteristic that contains common coils of hot rolled and cold-rolling property under the situation of high quality steel of 3.5% Si, also can improve manufacturing significantly, thereby the manufacturing process that can use common non-oriented electromagnetic steel sheet having.
Enumerate the example of representational manufacture method below.
At first, will be smelted into the molten steel of predetermined component, make plate slab by continuous metal cast process or ingot casting-cogging method by converter and secondary refining or electric furnace etc.
Then, on plate slab, implement hot rolling, but the outlet temperature in this hot rolling, the not special stipulation of coiling temperature, general condition, for example finishing temperature is that 700 ℃～900 ℃ and coiling temperature are to get final product about 400 ℃～800 ℃.
Then, as required, be purpose with the softening of steel plate and the magnetic properties that improves the finished product, can implement hot-rolled sheet annealing with the temperature about 600～1100 ℃.
Hot-rolled sheet annealing back (not implementing the back of reeling under the hot-rolled sheet annealed situation), implement cold rolling or warm-rolling and make the product thickness of slab (final thickness of slab) of regulation.Wherein, can form final thickness of slab, also can implement the cold rolling or warm-rolling more than the secondary of process annealing and form final thickness of slab by 1 cold rolling or warm-rolling.In addition, warm-rolling is usually with 100～300 ℃ of the rollings of steel billet temperature.
Wherein, final thickness of slab is preferably more than 0.15mm.
That is, thickness of slab is to the magnetic properties of product, and the influence of the iron loss characteristic of the high-frequency region when particularly using as the rotor material of high speed rotating motor more than important several 100Hz is bigger, considers that from this viewpoint thickness of slab is thin more favourable more.On the other hand, research product thickness of slab is to the result of the influence of mechanical characteristics, fatigue characteristic and magnetic properties generation, and the mechanical characteristics in the tension test is subjected to the influence of thickness of slab hardly, and with respect to this, fatigue characteristic sharply reduce when thinner than 0.15mm.And excessively thin-walled property is in motor manufacturing process, considers to become unfavorable in the aspect of the productivity that the increase during from the punching press perforator, the increase of lamination number cause.Therefore, under the situation of special attention fatigue strength, the lower limit of thickness of slab is preferably 0.15mm.And,, can suitably determine according to the rank of needed magnetic properties, but do below the normally used 0.65mm of being as electro-magnetic steel plate for the upper limit of thickness of slab.In addition, in the present invention, follow the deterioration of the magnetic properties of high strength, owing to suppress to such an extent that be lower than known in the past high-strength magnetic steel sheet, thereby make under the situation of equality strength rank, thickness of slab, can obtain than the good magnetic properties of steel in the past.
Then, with the above-mentioned final annealing of continuous annealing furnace, annealing conditions is separate provision in invention (1), (2) and invention (3), (4).
In invention (1), (2), importantly, with the unit cross-sectional area of steel band (with the vertical direction of steel plate direction of passage, the sectional area in so-called TD direction cross section) the stove internal tension on remains on more than the 2.5MPa, below the 20MPa, and carries out in the temperature range more than 700 ℃, below 850 ℃.By carrying out final annealing with above-mentioned condition to form the rolling coiled material that constitutes by steel of the present invention, the recovery organization of residual non-recrystallization in steel plate and can realize magnetic properties and high strength simultaneously, and web-shaped rectification effect fully.
That is, when 700 ℃ of annealing temperature less thaies or tension force deficiency 2.5MPa, shape correction is insufficient.On the other hand, when surpassing 850 ℃, owing to carrying out the reduction that recrystallize causes intensity.And, when the stove internal tension surpasses 20MPa, on coiled material, producing local deformaton, shape is variation on the contrary, or produces fracture in the stove, thereby 20MPa is made as the upper limit.From improving the viewpoint of steel plate shape, so preferred scope of work be final annealing temperature more than 750 ℃, below 850 ℃, stove internal tension be 5MPa above, below the 15MPa.
In addition, the annealing conditions of final annealing temperature etc. preferably is controlled to be the non-recrystallization recovery organization and guarantees more than 50% in area occupation ratio.In fact above-mentioned annealing conditions satisfies this requirement, but in steel under the situation of Ti quantity not sufficient 0.3%, from guaranteeing that more reliably the non-recrystallization recovery organization is the viewpoint more than 50%, preferably make the final annealing temperature T (℃) from Fig. 1 estimation and make it roughly satisfy following formula: T≤850-160 (0.3-x) (wherein, Ti amount in the x=steel: quality %).
On the other hand, in the present invention (3), (4), final annealing carries out in annealing temperature is scope more than 700 ℃, below 1050 ℃.During 700 ℃ of final annealing temperature less thaies, owing to can not fully carry out recrystallize, it is many that the non-recrystallization particle unnecessarily becomes, thereby shape correction becomes insufficient.And magnetic properties is also stable and become good more than 700 ℃ the time.Though iron loss characteristic improves along with the rising of annealing temperature, mechanical characteristics (endurance, tensile strength) and fatigue characteristic all manifest the trend of reduction, thereby annealing temperature can suitably determine according to needed magnetic properties rank and intensity rank.(viewpoint of the iron loss characteristic of 50～60Hz) to number kHz high-frequency region is than 900～1050 ℃ preferably 925～1025 ℃ from commercial frequency.But, when the final annealing temperature surpasses 1050 ℃, owing to not only can't see the improvement of magnetic properties, and cause the reduction of mechanical characteristics, energy aspect is also unfavorable, thereby the upper limit is limited to 1050 ℃.
And then above-mentioned final annealing by the coating and the sintering processes of treatment solution, is given steel plate with insulating coating, becomes the finished product.The kind of insulating coating, thickness or giving condition etc. are getting final product in the scope usually.For example be suitable for phosphoric acid salt overlay film etc.
(embodiment)
(embodiment 1: invention (1), (2))
After after becoming the plate slab be grouped into to be hot-rolled down to thickness of slab 2.5mm shown in the his-and-hers watches 1, implementing 900 ℃, keeping the hot-rolled sheet of 60s to anneal, carry out pickling and cold rolling till thickness of slab 0.35mm.
Here, the Ti amount surpasses the steel G of the scope of the invention owing in cold rolling back the squamous fold defect often takes place, thereby does not carry out later processing.And Si amount is high to 4.3%, contain the steel N of Ti and the steel P that the Si amount surpasses the scope of the invention hardly, because in cold rolling light plate fracture, thereby do not carry out later processing.Then, implement the final annealing of soaking time 20s with the condition shown in the table 2.In addition, the stove internal tension stove internal tension meter of opening roller mode by the survey of the load cell of packing in the bearing bottom is measured.
Table 1
Mechanical characteristics for this steel plate that obtains, utilize the JIS that cut out No. 5 tension test sheets parallel to estimate with rolling direction, for magnetic properties, take the Epstein test film (Epstein test pieces) of equivalent to estimate from rolling direction and rolling right angle orientation.
And, steel plate is sheared along rolling direction, grind its thick section and carry out structure observation, obtain the area ratio of recrystallized structure.For the tissue of final annealing temperature more than 500 ℃, regard the area of removing after the recrystallize part as the recovery organization ratio.
And, the planeness (flatness) of the steel plate before and after also annealing according to JIS C 2550 mensuration.
More than mensuration or evaluation result are illustrated in table 2 in the lump.
Table 2
| No. | Steel No. | The final annealing temperature (℃) | Stove internal tension (MPa) | Iron loss W 10/400 (W/kg) | Tensile strength TS (MPa) | Recovery organization ratio (%) | Recrystallized structure ratio (%) | Planeness (%) before the annealing | Annealing back planeness (%) | Remarks |
| 1 | A | 0 | ?5 | 105 | 990 | 0 | 0 | 3.6 | 3.6 | Comparative example |
| 2 | A | 400 | ?5 | 92 | 958 | 0 | 0 | 3.6 | 3.6 | Comparative example |
| 3 | A | 600 | ?5 | 53.5 | 832 | 100 | 0 | 3.6 | 3.4 | Comparative example |
| 4 | A | 650 | ?5 | 40 | 704 | 64 | 36 | 3.6 | 3.1 | Comparative example |
| 5 | A | 800 | ?5 | 22.5 | 550 | 0 | 100 | 3.5 | 1.9 | Comparative example |
| 6 | B | 700 | ?5 | 38 | 784 | 100 | 0 | 3.4 | 2.7 | Example |
| 7 | B | 800 | ?5 | 32 | 635 | 58 | 42 | 3.4 | 1.9 | Example |
| 8 | C | 700 | ?5 | 43 | 830 | 100 | 0 | 3.5 | 2.4 | Example |
| 9 | C | 800 | ?5 | 32.5 | 667 | 65 | 35 | 3.6 | 1.9 | Example |
| 10 | D | 700 | ?5 | 48 | 930 | 100 | 0 | 3.4 | 2.8 | Example |
| 11 | D | 800 | ?5 | 32.1 | 688 | 77 | 23 | 3.3 | 2.0 | Example |
| 12 | E | 700 | ?5 | 39 | 875 | 100 | 0 | 4.0 | 2.5 | Example |
| 13 | E | 750 | ?5 | 37 | 852 | 100 | 0 | 4.0 | 2.3 | Example |
| 14 | E | 800 | ?5 | 36 | 758 | 85 | 15 | 4.0 | 1.9 | Example |
| 15 | E | 850 | ?5 | 30 | 714 | 67 | 33 | 4.0 | 1.8 | Example |
| 15b | E | 870 | ?5 | 31 | 588 | 43 | 57 | 4.0 | 1.8 | Comparative example |
| 16 | E | 1000 | ?5 | 18 | 578 | 0 | 100 | 4.0 | 1.8 | Comparative example |
| 17 | F | 750 | ?5 | 45 | 939 | 100 | 0 | 4.2 | 2.1 | Example |
| 18 | F | 800 | ?5 | 38 | 821 | 84 | 16 | 4.0 | 1.8 | Example |
| 19 | F | 850 | ?5 | 31 | 745 | 70 | 30 | 3.9 | 1.7 | Example |
| 32 | H | 800 | ?5 | 37 | 810 | 75 | 25 | 4.2 | 2.1 | Example |
| 33 | I | 800 | ?5 | 29.2 | 562 | 32 | 68 | 4.2 | 1.9 | Comparative example |
| 34 | J | 800 | ?5 | 53 | 766 | 75 | 25 | 4.7 | 2.5 | Comparative example |
| 35 | K | 800 | ?5 | 44 | 751 | 73 | 27 | 4.1 | 2.0 | Example |
| 36 | L | 800 | ?5 | 39 | 830 | 70 | 30 | 4.6 | 2.1 | Example |
| 37 | M | 800 | ?5 | 35 | 866 | 78 | 22 | 4.4 | 2.1 | Example |
| 38 | O | 800 | ?5 | 39 | 818 | 75 | 25 | 4.2 | 1.9 | Example |
| 39 | Q | 800 | ?5 | 31.4 | 642 | 68 | 32 | 3.9 | 1.9 | Example |
| 40 | R | 800 | ?5 | 23.7 | 495 | 0 | 100 | 3.8 | 1.8 | Comparative example |
Annotate: steel G: the cold rolling squamous that takes place often folds, and does not carry out with aftertreatment
Steel N, P: because cold rolling time fracture is not carried out with aftertreatment
In table 2, the steel A that in the past formed as the No.1 of the rolling state of former material, carry out annealed No.2 for 400 ℃ with the recovery temperature of final annealing temperature no show steel, is made of 100% worked structure, though tensile strength is high, the remarkable variation of iron loss.And, be high strength with 600 ℃～650 ℃ annealing and the No.3 and the No.4 of residual recovery organization, iron loss also has improvement trend, but planeness almost do not improve before and after annealing, and the steel plate vpg connection is also not enough.On the other hand, non-recrystallization particulate area occupation ratio less than 50%, No.5, the 15b that the recrystallize particle becomes main body then intensity reduces significantly.And Ti amount does not reach among 16 times the No.33 of C+N and the No.41 and can not obtain full intensity in steel, and it is higher to surpass among 0.010% the No.34 iron loss at C+N.
With respect to this,, represent higher intensity and low iron loss, and the steel plate vpg connection is also good as using No.6～15,17～19,32,35～38 and 40 of forming the example of the steel that constitutes by steel of the present invention.
In addition, Si measures above 4.0% in the steel No.37 and Si+Al amount surpass 4.0% No.38, and the curved characteristic after the hot-rolled sheet annealing is respectively 27 times and 23 times.With respect to this, all more than 40 times, manufacturing is better for other examples.Here, curved characteristic carries out the repeated flex test of 90 ° of bending radius 15mm, angle of bend, to estimate up to the number of times till steel plate generation crackle in 30 ℃ of temperature.
(embodiment 2: invention (1), (2))
After after the steel A of his-and-hers watches 1 and the slab of D are hot-rolled down to thickness of slab 2.5mm, implementing 800 ℃, keeping the hot-rolled sheet annealing of 60s, carry out pickling and cold rolling till thickness of slab 0.35mm, make coiled material.Resulting coiled material is carried out the final annealing that carries out with continuous annealing furnace with the condition shown in the table 3, carry out the evaluation identical with embodiment 1.
Its result is recorded in shown in the table 3 in the lump.As known from Table 3, steel A and D are under lower 650 ℃ of annealing temperature, even all be that the stove internal tension is higher, the improvement degree of steel plate shape is also less.On the other hand, annealing temperature is increased to 800 ℃ and with the steel plate shape of stove internal tension control coiled material within the scope of the present invention, significantly improve.By this final annealing, intensity reduces and becomes big in steel A in the past, is not enough to use as High Strength Steel, with respect to this, in the steel D as example of the present invention, can realize high strength and good steel plate shape simultaneously.
In addition, surpass at the stove internal tension under the situation of the 20MPa that is fit to range limit, iron loss increases, and the steel plate shape is variation also.
Table 3
| No. | Steel No. | The final annealing temperature (℃) | Stove internal tension (MPa) | Iron loss W 10/400 (W/kg) | Tensile strength TS (MPa) | Recovery organization ratio (%) | Recrystallized structure ratio (%) | Planeness (%) before the annealing | Annealing back planeness (%) | Remarks |
| 20 | A | 650 | ?5 | 40.1 | 704 | 65 | 35 | 3.6 | 3.1 | Comparative example |
| 21 | A | 650 | ?15 | 39.5 | 701 | 63 | 37 | 3.6 | 2.8 | Comparative example |
| 22 | A | 800 | ?5 | 22.5 | 550 | 0 | 100 | 3.5 | 1.9 | Comparative example |
| 23 | A | 800 | ?15 | 21.7 | 548 | 0 | 100 | 3.6 | 1.4 | Comparative example |
| 24 | |
650 | ?5 | 61.3 | 998 | 100 | 0 | 3.4 | 3.1 | Example |
| 25 | |
650 | ?20 | 62.3 | 1009 | 100 | 0 | 3.4 | 2.6 | Example |
| 26 | |
800 | 1.5 | 32.3 | 681 | 78 | 22 | 3.4 | 2.8 | Example (manufacture method is not suitable for) |
| 27 | |
800 | ?5 | 32.1 | 688 | 77 | 23 | 3.3 | 2.0 | Example |
| 28 | |
800 | ?10 | 31.9 | 685 | 75 | 25 | 3.4 | 1.7 | Example |
| 29 | |
800 | ?15 | 31.9 | 679 | 78 | 22 | 3.4 | 1.6 | Example |
| 30 | |
800 | ?20 | 32.5 | 682 | 78 | 22 | 3.4 | 1.6 | Example |
| 31 | |
800 | 23 | 37.8 | 680 | 78 | 22 | 3.4 | 2.2 | Example (manufacture method is not suitable for) |
(embodiment 3: invention (1), (2))
Become the plate slab be grouped into to carry out cold rolling till final thickness of slab shown in the his-and-hers watches 4 with the arbitrary condition among the following a to c.
A: after being hot-rolled down to thickness of slab 2.0mm, do not implement hot-rolled sheet annealing, warm-rolling is to final thickness of slab 0.35mm (steel billet temperature is 250 ℃).
B: after being hot-rolled down to thickness of slab 3.8mm, do not implement hot-rolled sheet annealing, be cold-rolled to 1.5mm, implement then 1000 ℃-keep the process annealing of 30s after, be cold-rolled to final thickness of slab 0.35mm.
C: after being hot-rolled down to thickness of slab 2.5mm, implement 1050 ℃-keep the hot-rolled sheet annealing of 30s after, be cold-rolled to 1.0mm, implement then 1000 ℃-keep the process annealing of 30s after, warm-rolling is to final thickness of slab 0.20mm (steel billet temperature is 200 ℃).
Then, implementing soaking time with the condition shown in the table 5 is the final annealing of 10s, carries out the evaluation identical with embodiment 1, and its result is illustrated in the table 5 in the lump.Each steel of the present invention is realized good intensity and magnetic properties simultaneously.
Table 4
Table 5
| No. | Steel No. | Rolling condition | The final annealing temperature (℃) | Stove internal tension (MPa) | Iron loss W 10/400 (W/kg) | Tensile strength TS (MPa) | Recovery organization ratio (%) | Recrystallized structure ratio (%) | Planeness (%) before the annealing | Annealing back planeness (%) | Remarks |
| 42 | S | a | 800 | 10 | 33.5 | 768 | 77 | 23 | 3.8 | 2.0 | Example |
| 43 | T | a | 770 | 10 | 35 | 785 | 89 | 11 | 3.9 | 2.2 | Example |
| 44 | U | a | 850 | 10 | 32 | 707 | 60 | 40 | 3.9 | 1.8 | Example |
| 45 | V | |
800 | 15 | 33 | 772 | 74 | 26 | 3.9 | 2.0 | Example |
| 46 | W | b | 720 | 15 | 42 | 840 | 100 | 0 | 3.6 | 2.0 | Example |
| 47 | X | c | 780 | 15 | 28 | 855 | 88 | 12 | 4.1 | 1.9 | Example |
| 48 | Y | c | 720 | 15 | 25 | 924 | 100 | 0 | 4.2 | 2.1 | Example |
(embodiment 4: invention (3), (4))
To by becoming shown in the table 6 to be grouped into the plate slab that constitutes, be hot-rolled down to thickness of slab 2mm after, after implementing 900 ℃, keeping the hot-rolled sheet annealing of 60s, carry out pickling, then be cold-rolled to thickness of slab 0.35mm after, implement 950 ℃, the final annealing of maintenance 30s.
At this moment, the hot-roll annealing plate being cut out with the 30mm width, is that 30 ℃ of enforcement bending radius are that 15mm, angle of bend are 90 repeated flex test (repetition bending test) with temperature, and the steel plate trafficability characteristic on the manufacturing line is carried out Simulation evaluation.° and, as the evaluation of cold-rolling property, the degree of depth is split on the limit of having measured the rolled sheet material end face.
Will be for mechanical characteristics (tensile strength TS), fatigue characteristic (safe range of stress intensity FS) and magnetic properties (the magneticflux-density B of the electro-magnetic steel plate that obtains like this
50, high frequency iron loss W
10/1000) result that investigates, be documented in the table 7.
Wherein, the evaluation method of each characteristic is as follows:
Mechanical characteristics uses No. 5 tension test sheets of JIS that cut out abreast with rolling direction to estimate.
Fatigue characteristic are following to be estimated: cut out test film abreast with rolling direction, utilize No. 800 sand paper to grind to the parallel portion end face after, with stress ratio: the part of 0.1, frequency: 20Hz stretch (stretching-stretching) carry out, by through 1,000 ten thousand (10
7) maximum stress (safe range of stress intensity FS) that also can not produce the steel plate fracture after the circulation estimates.
Magnetic properties takes the Epstein test film of equivalent to estimate from rolling direction and rolling right angle orientation.
Table 6
Table 7
| Steel | Hot-rolled sheet number of bends (inferior) | Cold rolling edges of boards split the degree of depth (mm) | TS (MPa) | FS (MPa) | B 50 (T) | ?W 10/1κ?(W/kg) | Remarks |
| 1 | 4.0 | 3.7 | 621 | 528 | 1.69 | ?78 | Comparative example |
| 2 | 3.8 | 1.4 | 630 | 529 | 1.69 | ?79 | Comparative example |
| 3 | 8.2 | 1.1 | 671 | 570 | 1.67 | ?83 | Comparative example |
| 4 | 24.5 | 0.4 | 669 | 575 | 1.67 | ?84 | Example |
| 5 | 28.8 | 0.2 | 697 | 599 | 1.66 | ?86 | Example |
| 6 | 29.0 | 0.3 | 756 | 643 | 1.64 | ?92 | Example |
| 7 | 31.0 | 0.4 | 825 | 701 | 1.63 | ?96 | Example |
| 8 | 28.0 | 0.4 | 919 | 772 | 1.60 | ?104 | Example |
| 9 | 8.5 | 5.0 | 1090 | 850 | 1.56 | ?122 | Comparative example |
| 10 | 3.0 | 5.4 | 632 | 525 | 1.69 | ?83 | Comparative example |
| 11 | 3.0 | 4.1 | 635 | 545 | 1.67 | ?88 | Comparative example |
| 12 | 5.5 | 3.5 | 695 | 570 | 1.66 | ?95 | Comparative example |
| 13 | 10.4 | 1.3 | 735 | 610 | 1.66 | ?96 | Comparative example |
| 14 | 23.9 | 0.7 | 755 | 634 | 1.65 | ?99 | Example |
| 15 | 24.8 | 0.5 | 799 | 687 | 1.64 | ?106 | Example |
| 16 | 26.5 | 0.7 | 950 | 808 | 1.60 | ?119 | Example |
| 17 | 9.0 | 0.6 | 1050 | 872 | 1.58 | ?129 | Comparative example |
| 18 | 7.0 | 5.6 | 1220 | 1000 | 1.52 | ?159 | Comparative example |
| 19 | 1.0 | 9.0 | 638 | 523 | 1.68 | ?95 | Comparative example |
| 20 | 0.5 | 9.0 | 680 | 537 | 1.67 | ?117 | Comparative example |
| 21 | 2.0 | 6.2 | 715 | 551 | 1.64 | ?144 | Comparative example |
| 22 | 2.6 | 5.0 | 791 | 593 | 1.61 | ?153 | Comparative example |
| 23 | 7.2 | 3.5 | 853 | 631 | 1.59 | ?161 | Comparative example |
| 24 | 11.9 | 3.1 | 1006 | 734 | 1.55 | ?180 | Comparative example |
| 25 | 6.2 | 4.8 | 1080 | 778 | 1.53 | ?182 | Comparative example |
| 26 | 3.9 | 6.8 | 1195 | 848 | 1.50 | ?191 | Comparative example |
| 27 | 1.0 | 9.0 | 651 | 508 | 1.67 | ?118 | Comparative example |
| 28 | 0.5 | 9.0 | 733 | 535 | 1.64 | ?159 | Comparative example |
| 29 | 1.4 | 9.0 | 855 | 581 | 1.61 | ?190 | Comparative example |
| 30 | 0.5 | 5.8 | 1000 | 610 | 1.59 | ?224 | Comparative example |
| 31 | 3.4 | 4.5 | 1065 | 660 | 1.57 | ?229 | Comparative example |
| 32 | 7.2 | 4.3 | 1138 | 694 | 1.55 | ?239 | Comparative example |
| 33 | 1.5 | 6.7 | 1218 | 706 | 1.53 | ?243 | Comparative example |
| 58 | 76 | 0.1 | 587 | 464 | 1.66 | ?117 | Comparative example |
| 59 | 43 | 0.3 | 762 | 609 | 1.65 | ?101 | Example |
Shown in chart 7, as can be known according to the present invention, make Si surpass 3.5%, control C, N amount, and the example of adding an amount of Ti all are that manufacturing is good, have advantages of higher tensile strength and safe range of stress, and can obtain good magnetic properties.
(embodiment 5: invention (3), (4))
To by becoming shown in the table 8 to be grouped into the plate slab that constitutes, be hot-rolled down to thickness of slab 2mm after, after implementing 900 ℃, keeping the hot-rolled sheet annealing of 60s, carry out pickling, then be cold-rolled to thickness of slab 0.25mm after, implement 950 ℃, the final annealing of maintenance 30s.
At this moment, the hot-roll annealing plate being cut out with the 30mm width, is that 30 ℃ of enforcement bending radius are that 15mm, angle of bend are 90 repeated flex test with temperature, and the steel plate trafficability characteristic on the manufacturing line is carried out Simulation evaluation.° and, as the evaluation of cold-rolling property, the degree of depth is split on the limit of having measured the rolled sheet material end face.
Will be for mechanical characteristics (tensile strength TS), fatigue characteristic (safe range of stress intensity FS) and magnetic properties (the magneticflux-density B of the electro-magnetic steel plate that obtains like this
50, high frequency iron loss W
10/1000) result that investigates, be illustrated in the table 9.
Table 9
| Steel | Hot-rolled sheet number of bends (inferior) | Cold rolling edges of boards split the degree of depth (mm) | TS (MPa) | FS (MPa) | B 50 (T) | W 10/1κ (W/kg) | Remarks |
| 34 | 6.4 | 4.7 | 602 | 457 | 1.69 | 115 | Comparative example |
| 35 | 37 | 0.2 | 765 | 650 | 1.65 | 71 | Example |
| 36 | 34 | 0.6 | 790 | 672 | 1.64 | 72 | Example |
| 37 | 32.5 | 0.7 | 795 | 684 | 1.64 | 72 | Example |
| 38 | 27.5 | 0.9 | 843 | 717 | 1.62 | 72 | Example |
| 39 | 19 | 0.9 | 870 | 731 | 1.61 | 77 | Example |
| 40 | 5.3 | 2.9 | 910 | 564 | 1.60 | 81 | Comparative example |
| 41 | 2.2 | 5.4 | 1025 | 574 | 1.57 | 85 | Comparative example |
| 42 | 15.2 | 0.6 | 764 | 634 | 1.65 | 102 | Example |
| 43 | 22.2 | 0.5 | 778 | 661 | 1.59 | 63 | Example |
| 44 | 26 | 0.7 | 769 | 661 | 1.65 | 61 | Example |
| 45 | 23.3 | 0.5 | 840 | 772 | 1.64 | 69 | Example |
| 46 | 20.5 | 0.4 | 957 | 818 | 1.63 | 72 | Example |
| 60 | 5.5 | 6.4 | 631 | 538 | 1.68 | 74 | Comparative example |
| 61 | 28.3 | 0.8 | 736 | 604 | 1.65 | 72 | Example |
| 62 | 3.5 | 5.1 | 1010 | 688 | 1.51 | 86 | Comparative example |
As shown in table 9, as can be known the steel plate Composition Control is satisfied C of the present invention, N amount, and adding an amount of Ti, the example of V, all be that manufacturing is good, have advantages of higher tensile strength and safe range of stress, and can obtain good magnetic properties.
On the other hand, the addition of Si surpasses at 5% o'clock, and is big although the reduction of the bendability of hot-rolled steel sheet, cold-rolling property becomes, and tensile strength is higher, and safe range of stress intensity shows the trend that reduces.
(embodiment 6: invention (3), (4))
To by becoming shown in the table 10 to be grouped into the plate slab that constitutes, be hot-rolled down to thickness of slab 2.2mm after, after implementing 800 ℃, keeping the hot-rolled sheet annealing of 90s, carry out pickling, then be cold-rolled to thickness of slab 0.30mm after, implement 1000 ℃, the final annealing of maintenance 30s.Only No.67 omits hot-rolled sheet annealing, adopts to be hot-rolled down to thickness of slab 3.0mm → do not have hot-rolled sheet annealing → warm-rolling to thickness of slab 1.5mm (steel billet temperature is 280 ℃) → 900 ℃-30s process annealing → be cold-rolled to rolling process of final thickness of slab 0.30mm.
In addition, hot-roll annealing steel plate (No.67 is a hot-rolled steel sheet) being cut out with the 30mm width, is that 30 ℃ of enforcement bending radius are that 15mm, angle of bend are 90 ° repeated flex test with temperature, and the steel plate trafficability characteristic on the manufacturing line is carried out Simulation evaluation.And as the evaluation of cold-rolling property, the degree of depth is split on the limit of having measured the rolled sheet material end face.
Will be for mechanical characteristics (tensile strength TS), fatigue characteristic (safe range of stress intensity FS) and magnetic properties (the magneticflux-density B of the electro-magnetic steel plate that obtains like this
50, high frequency iron loss W
10/1000) result that investigates, be illustrated in the table 11.
Table 11
| Steel | Hot-rolled sheet number of bends (inferior) | Cold rolling edges of boards split the degree of depth (mm) | TS (MPa) | FS (MPa) | B 50 (T) | ?W 10/1κ?(W/kg) | Remarks |
| 47 | 2.5 | 5.0 | 678 | 502 | 1.66 | ?71 | Comparative example |
| 48 | 23.6 | 1.2 | 706 | 551 | 1.65 | ?73 | Example |
| 49 | 22.1 | 0.9 | 758 | 599 | 1.64 | ?74 | Example |
| 50 | 17.1 | 1.7 | 862 | 672 | 1.61 | ?74 | Example |
| 51 | 6.2 | 6.3 | 1055 | 749 | 1.55 | ?82 | Comparative example |
| 52 | 16.5 | 0.9 | 855 | 668 | 1.61 | ?76 | Example |
| 53 | 12.0 | 0.9 | 887 | 691 | 1.60 | ?77 | Example |
| 63 | 26.5 | 0.4 | 808 | 701 | 1.62 | ?76 | Example |
| 64 | 1.0 | 12.5 | 576 | 389 | 1.62 | ?78 | Comparative example |
| 65 | 18.3 | 0.6 | 723 | 586 | 1.62 | ?74 | Example |
| 66 | 6.5 | 4.5 | 660 | 461 | 1.55 | ?83 | Comparative example |
| 67* | 43.5 | 0.4 | 903 | 710 | 1.58 | ?78 | Example |
*) be hot-rolled down to thickness of slab 3.0mm → do not have hot-rolled sheet annealing → warm-rolling to the final thickness of slab 0.30mm of thickness of slab 1.5mm (steel billet temperature is 280 ℃) → 900 ℃-30s process annealing → be cold-rolled to.
Shown in chart 11, as can be known the steel plate Composition Control is being satisfied C of the present invention, N amount, and add an amount of Nb, Zr or and then the example of adding Ti, V, all be that manufacturing is good, have advantages of higher tensile strength and safe range of stress, and have good magnetic properties.
(embodiment 7: invention (3), (4))
To forming the plate slab that steel of the present invention is formed with 3.9%Si, 0.14%Mn, 0.33%Al, 2.67%Ni, 0.02%P, 0.002%S, 0.0009%C, 0.0018%N, 0.28%Ti and 0.055Sn (Ti/ (C+N)=103.7), after being hot-rolled down to thickness of slab 2mm, after implementing 1000 ℃, keeping the hot-rolled sheet annealing of 60s, carry out pickling, after then being cold-rolled to various thicknesss of slab, implement 950 ℃, keep the final annealing of 30s, the influence that each characteristic produces is investigated for thickness of slab.
Resulting result is as shown in table 12.
Table 12
| Steel | Thickness of slab (mm) | ?TS(MPa) | ?FS(MPa) | B 50(T) | W 10/1κ(W/kg) | Remarks |
| 54 | 0.35 | ?776 | ?667 | 1.65 | 91.0 | Example |
| 55 | 0.20 | ?781 | ?656 | 1.65 | 52.4 | Example |
| 56 | 0.15 | ?769 | ?638 | 1.65 | 44.2 | Example |
| 57 | 0.11 | ?782 | ?555 | 1.65 | 39.4 | Example (it is outer to be fit to scope) |
As shown in table 12, by making the thickness of slab attenuation high frequency iron loss characteristic is greatly improved.
And tensile strength is all roughly the same for any thickness of slab.
But safe range of stress intensity is that 0.15mm significantly improves when above at thickness of slab.
Industrial applicibility
According to the present invention, form or further limit tissue by determinant, can not append restriction in the steel plate manufacturing or new operation and stably obtain high strength or and then material of excellent fatigue characteristics and steel plate shape and all good non-oriented electromagnetic steel sheet having of magnetic properties.
Claims (3)
1. highly strong, non-oriented electrical steel sheet wherein, has following compositions and forms:
In quality %,
With C and N suppress for below the C:0.010% and below the N:0.010%,
And C+N≤0.010% contains
More than the Si:1.5%, below 4.0%, below the Mn:3.0%,
Al:3.0% is following, P:0.2% is following,
Below the S:0.01%,
And contain more than the Ti:0.05% in the scope that satisfies Ti/ (C+N) 〉=16, below 0.8%,
Surplus is Fe and unavoidable impurities;
And the ratio that exists of the non-recrystallization recovery organization in the steel plate is counted more than 50% with area occupation ratio.
2. highly strong, non-oriented electrical steel sheet as claimed in claim 1, wherein, in quality %, also contain at least a kind that is selected from Ni:0.1～5.0%, Sb:0.002～0.1%, Sn:0.002～0.1%, B:0.001～0.01%, Ca:0.001～0.01%, Rem:0.001～0.01% and Co:0.2～5.0%.
3. the manufacture method of a highly strong, non-oriented electrical steel sheet, wherein, carry out hot rolling to having the plate slab that following compositions forms:
In quality %,
With C and N suppress for below the C:0.010% and below the N:0.010%,
And C+N≤0.010% contains
More than the Si:1.5%, below 5.0%, below the Mn:3.0%,
Al:3.0% is following, P:0.2 quality % is following,
Below the S:0.01 quality %,
And contain more than the Ti:0.05 quality % in the scope that satisfies Ti/ (C+N) 〉=16, below the 0.8 quality %;
Then, form the cold rolling coiled material of final thickness of slab by cold rolling or warm-rolling after,
When carrying out final annealing, with this final annealing in annealing temperature be more than 700 ℃, below 850 ℃, the stove internal tension is to carry out more than the 2.5MPa, below the 20MPa.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005362020 | 2005-12-15 | ||
| JP361995/2005 | 2005-12-15 | ||
| JP362020/2005 | 2005-12-15 | ||
| JP2005361995 | 2005-12-15 | ||
| PCT/JP2006/325319 WO2007069776A1 (en) | 2005-12-15 | 2006-12-13 | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
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| CN 201110159667 Division CN102226251B (en) | 2005-12-15 | 2006-12-13 | Highly strong, non-oriented electrical steel sheet and method for manufacture thereof |
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| CN101310034B true CN101310034B (en) | 2011-12-28 |
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| KR (1) | KR101011965B1 (en) |
| CN (2) | CN101310034B (en) |
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| CN102292462A (en) * | 2009-01-26 | 2011-12-21 | 新日本制铁株式会社 | Non-oriented electromagnetic steel sheet |
| CN102459675B (en) * | 2009-06-03 | 2016-06-01 | 新日铁住金株式会社 | Non-oriented electromagnetic steel sheet having and manufacture method thereof |
| JP5854182B2 (en) * | 2010-08-30 | 2016-02-09 | Ｊｆｅスチール株式会社 | Method for producing non-oriented electrical steel sheet |
| US20130306200A1 (en) * | 2011-02-24 | 2013-11-21 | Jfe Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing the same |
| CN102274936B (en) * | 2011-08-03 | 2013-03-13 | 东北大学 | Method for manufacturing non-oriented silicon steel plate based on twin-roll thin strip continuous casting technology |
| JP5263363B2 (en) * | 2011-10-11 | 2013-08-14 | Ｊｆｅスチール株式会社 | Method for producing non-oriented electrical steel sheet |
| EP2612942B1 (en) * | 2012-01-05 | 2014-10-15 | ThyssenKrupp Steel Europe AG | Non-grain oriented electrical steel or sheet metal, component produced from same and method for producing non-grain oriented electrical steel or sheet metal |
| IN2015DN00288A (en) * | 2012-08-08 | 2015-06-12 | Jfe Steel Corp | |
| JP6127408B2 (en) | 2012-08-17 | 2017-05-17 | Ｊｆｅスチール株式会社 | Method for producing non-oriented electrical steel sheet |
| CN104674136B (en) * | 2013-11-28 | 2017-11-14 | Posco公司 | The excellent non-oriented electromagnetic steel sheet of permeability and its manufacture method |
| JP6319574B2 (en) * | 2014-08-14 | 2018-05-09 | Ｊｆｅスチール株式会社 | Non-oriented electrical steel sheet with excellent magnetic properties |
| EP3594371B1 (en) | 2017-03-07 | 2021-07-07 | Nippon Steel Corporation | Non-oriented electrical steel sheet and method for manufacturing non-oriented electrical steel sheet |
| EP3656885A4 (en) | 2017-07-19 | 2021-04-14 | Nippon Steel Corporation | Non-oriented electromagnetic steel plate |
| BR112020018565A2 (en) * | 2018-03-20 | 2020-12-29 | Nippon Steel Corporation | PRODUCTION METHOD FOR MANUFACTURING GRAIN ORIENTED ELECTRIC STEEL SHEET AND ORIENTED GRAIN ELECTRIC STEEL SHEET |
| US11661636B2 (en) * | 2018-03-20 | 2023-05-30 | Nippon Steel Corporation | Method for manufacturing grain-oriented electrical steel sheet and grain-oriented electrical steel sheet |
| KR102325011B1 (en) * | 2019-12-20 | 2021-11-11 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
| EP4108790A1 (en) * | 2020-02-20 | 2022-12-28 | Nippon Steel Corporation | Steel sheet for non-oriented electromagnetic steel sheet |
| US20230137498A1 (en) * | 2020-04-16 | 2023-05-04 | Nippon Steel Corporation | Non-oriented electrical steel sheet and method of manufacturing the same |
| KR20230096881A (en) * | 2021-12-22 | 2023-06-30 | 주식회사 포스코 | Non-oriented electrical steel sheet and method for manufacturing the same |
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| JP2853552B2 (en) * | 1994-02-01 | 1999-02-03 | 住友金属工業株式会社 | Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method |
| CN1278016A (en) * | 1999-06-16 | 2000-12-27 | 住友金属工业株式会社 | Non-directional electromagnetic steel sheet, and method for mfg. same |
| JP2005298935A (en) * | 2004-04-14 | 2005-10-27 | Nippon Steel Corp | Method for producing non-oriented silicon steel sheet excellent in whole peripheral magnetic characteristic and punch-out workability |
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| JP4546713B2 (en) * | 2003-10-06 | 2010-09-15 | 新日本製鐵株式会社 | Final product of high-strength electrical steel sheet with excellent magnetic properties, its use and manufacturing method |
| JP4389691B2 (en) * | 2004-06-22 | 2009-12-24 | 住友金属工業株式会社 | Non-oriented electrical steel sheet for rotor and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2853552B2 (en) * | 1994-02-01 | 1999-02-03 | 住友金属工業株式会社 | Non-oriented electrical steel sheet with excellent magnetic properties and manufacturing method |
| CN1278016A (en) * | 1999-06-16 | 2000-12-27 | 住友金属工业株式会社 | Non-directional electromagnetic steel sheet, and method for mfg. same |
| JP2005298935A (en) * | 2004-04-14 | 2005-10-27 | Nippon Steel Corp | Method for producing non-oriented silicon steel sheet excellent in whole peripheral magnetic characteristic and punch-out workability |
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| CN102226251A (en) | 2011-10-26 |
| WO2007069776A1 (en) | 2007-06-21 |
| TWI312371B (en) | 2009-07-21 |
| KR20080063521A (en) | 2008-07-04 |
| CN102226251B (en) | 2012-12-12 |
| CN101310034A (en) | 2008-11-19 |
| KR101011965B1 (en) | 2011-01-31 |
| TW200730642A (en) | 2007-08-16 |
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