CN107002196A - Magnetic pole is with hot rolled steel plate and its manufacture method and hydroelectric generation rim component - Google Patents
Magnetic pole is with hot rolled steel plate and its manufacture method and hydroelectric generation rim component Download PDFInfo
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- CN107002196A CN107002196A CN201580065641.8A CN201580065641A CN107002196A CN 107002196 A CN107002196 A CN 107002196A CN 201580065641 A CN201580065641 A CN 201580065641A CN 107002196 A CN107002196 A CN 107002196A
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- steel plate
- rolled steel
- hot rolled
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 93
- 239000010959 steel Substances 0.000 title claims abstract description 93
- 238000000034 method Methods 0.000 title claims abstract description 34
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 17
- 230000004907 flux Effects 0.000 claims abstract description 37
- 238000005096 rolling process Methods 0.000 claims abstract description 37
- 238000001556 precipitation Methods 0.000 claims abstract description 24
- 238000003466 welding Methods 0.000 claims abstract description 22
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 14
- 229910052751 metal Inorganic materials 0.000 claims abstract description 11
- 239000002184 metal Substances 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 239000000203 mixture Substances 0.000 claims description 26
- 229910052719 titanium Inorganic materials 0.000 claims description 19
- 238000007747 plating Methods 0.000 claims description 18
- 239000000463 material Substances 0.000 claims description 17
- 238000012545 processing Methods 0.000 claims description 15
- 229910052720 vanadium Inorganic materials 0.000 claims description 14
- 238000005098 hot rolling Methods 0.000 claims description 11
- 229910052725 zinc Inorganic materials 0.000 claims description 11
- 239000011701 zinc Substances 0.000 claims description 11
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 8
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 7
- 239000011248 coating agent Substances 0.000 claims description 6
- 238000000576 coating method Methods 0.000 claims description 6
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 230000015572 biosynthetic process Effects 0.000 claims 1
- 239000012535 impurity Substances 0.000 abstract description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 20
- 229910001567 cementite Inorganic materials 0.000 description 15
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 15
- 238000012360 testing method Methods 0.000 description 9
- 230000009467 reduction Effects 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 239000013078 crystal Substances 0.000 description 6
- 229910001335 Galvanized steel Inorganic materials 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 239000008397 galvanized steel Substances 0.000 description 5
- 238000005246 galvanizing Methods 0.000 description 5
- 230000007704 transition Effects 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 4
- 239000003792 electrolyte Substances 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000005868 electrolysis reaction Methods 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000003723 Smelting Methods 0.000 description 2
- YRKCREAYFQTBPV-UHFFFAOYSA-N acetylacetone Chemical compound CC(=O)CC(C)=O YRKCREAYFQTBPV-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 238000004364 calculation method Methods 0.000 description 2
- 229910002092 carbon dioxide Inorganic materials 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000007598 dipping method Methods 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 230000009931 harmful effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000001095 inductively coupled plasma mass spectrometry Methods 0.000 description 2
- 239000010813 municipal solid waste Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 238000009849 vacuum degassing Methods 0.000 description 2
- 238000010792 warming Methods 0.000 description 2
- 241000219307 Atriplex rosea Species 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- OKIZCWYLBDKLSU-UHFFFAOYSA-M N,N,N-Trimethylmethanaminium chloride Chemical class [Cl-].C[N+](C)(C)C OKIZCWYLBDKLSU-UHFFFAOYSA-M 0.000 description 1
- 229910001327 Rimmed steel Inorganic materials 0.000 description 1
- 238000007545 Vickers hardness test Methods 0.000 description 1
- 238000003556 assay Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 230000001427 coherent effect Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005244 galvannealing Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 238000005476 soldering Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- 230000003245 working effect Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
-
- 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
-
- 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
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- 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
- H01F1/18—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 with insulating coating
-
- H—ELECTRICITY
- H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
- H02K—DYNAMO-ELECTRIC MACHINES
- H02K1/00—Details of the magnetic circuit
- H02K1/02—Details of the magnetic circuit characterised by the magnetic material
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E10/00—Energy generation through renewable energy sources
- Y02E10/20—Hydro energy
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Thermal Sciences (AREA)
- Power Engineering (AREA)
- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Crystallography & Structural Chemistry (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Dispersion Chemistry (AREA)
- Soft Magnetic Materials (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
The present invention provides the magnetic pole of high intensity and weldability and excellent in magnetic characteristics with hot rolled steel plate and its manufacture method, hydroelectric generation rim component.Contain C：More than 0.02% and less than 0.12%, Si：More than 0.1% and less than 0.7%, Mn：More than 0.8% and less than 1.6%, P：Less than 0.03%, S：Less than 0.005%, Al：Less than 0.08%, N：Less than 0.006%, Nb：More than 0.06% and less than 0.20%, surplus is made up of Fe and inevitable impurity.Ferritic phase is calculated as more than 98% with area occupation ratio, the Fe of precipitation is below 0.22 mass % relative to Fe amounts contained in steel, the Nb of precipitation is more than 80 mass % relative to Nb amounts contained in steel, the average grain diameter of the carbide containing Nb separated out is below 6nm, the yield strength of rolling direction is more than 500MPa, magnetic flux density B50For more than 1.4T, magnetic flux density B100For more than 1.5T, the minimum of the Vickers hardness of welding heat affected zone is more than (average value 30 of the Vickers hardness of mother metal).
Description
Technical field
The present invention relates to the magnetic pole hot rolled steel plate and its manufacture method for being suitable for hydroelectric generation rim component etc. and
Hydroelectric generation rim component.
Background technology
In recent years, from the viewpoint of the saving from damage of earth environment, global warming is considered as problem, does not discharge carbon dioxide gas
Increase the need for the natural energy resources of body.In addition, from the viewpoint of such global warming is suppressed, recently as clean energy resource
Hydroelectric generation be considered as wish.The generators such as hydroelectric generator possess rotor and stator, the magnetic that rotor is acted on by performance iron core
Pole iron core (pole core) and the wheel rim composition for supporting the pole core.In order to obtain generating capacity, it is necessary to make rotor rotation at a high speed
Turn.Therefore, high intensity is kept for wheel rim requirement in order to bear the centrifugal force of rotation at a high speed.In addition, being used simultaneously for wheel rim
Steel plate (rim component) requires to keep excellent magnetic characteristic.In addition, steel plate is engaged each other by welding, but the intensity of weld part
Easily change, therefore, also require that weldability (weldability) is excellent.
Above-mentioned requirements are answered, up to the present, the hot rolled steel plate for being conceived to magnetic characteristic, weldability, it is proposed that various skills
Art.
For example, in patent document 1, by with including the ferritic phase (ferrite that area occupation ratio is more than 95%
Phase) and in the crystal grain (crystal grain) of the ferritic phase it is precipitated with average grain diameter and contains Ti and V less than 10nm
Precipitate (precipitate) tissue and the average crystallite particle diameter of the ferritic phase is set as 2 μm less than 10 μ
In the range of m, intensity and magnetic flux density B that the yield strength with rolling direction is more than 700MPa can be obtained50For 1.5T
Above, B100For the steel plate of more than 1.6T electromagnetic property.
In patent document 2, C will be contained in terms of weight %：0.05~0.15%, Si：Less than 0.5%, Mn：0.70~
2.00%th, Ti：0.10~0.30%, B：0.0015~0.0050% steel plate is batched after carrying out hot rolling below 500 DEG C,
Thus, it is possible to obtain the high-tension hot rolled steel plate with high magnetic flux density.
Patent Document 3 discloses a kind of whirler (rotator) iron core high working property high tensile hot rolled steel sheet, its
In, contain C≤0.10%, Ti：0.02~0.2%, further containing at least one of Mo≤0.7%, W≤1.5%, essence
On be dispersed with ferritic structure containing Ti, with least one of the Mo and W carbide less than 10nm, with 590MPa
Intensity more than level.
Prior art literature
Patent document
Patent document 1：International Publication No. 2013/115205
Patent document 2：Japanese Unexamined Patent Application 63-166931 publications
Patent document 3：Japanese Unexamined Patent Publication 2003-268509 publications
The content of the invention
Invent problem to be solved
But, in the technology proposed in patent document 1, due to containing solid solution V (solute V), therefore, analysing thickly
The control of cementite (cementite) amount gone out is extremely difficult, and then weldability is deteriorated.
, it is necessary in the unmanageable temperature model that coiling temperature is less than 500 DEG C in the technology proposed in patent document 2
Enclose it is interior batched, between coiled material and coiled material in characteristic deviation turn into problem.In addition, low temperature phase change phase factor phase transition strain is not
The deterioration of plate shape caused by uniform and be not suitable as wheel rim component.
In the technology proposed in patent document 3, do not accounted for not only for weldability, and for thick cementite
Influence do not account for yet, it is thus impossible to the magnetic characteristic stablized.
In view of the foregoing, it is more than 500MPa and welding it is an object of the invention to provide the yield strength of rolling direction
The magnetic pole of property and excellent in magnetic characteristics is with hot rolled steel plate and its manufacture method and hydroelectric generation rim component.
Method for solving problem
For high intensity and have good weldability concurrently and the condition of the steel plate of good magnetic characteristic has made intensive studies,
As a result find, the hardness reduction in welding heat affected zone (heat-affected zone) is by big being carbonized containing V of solubility
The influence that the dissolving (re-solution) of thing is brought is larger.And it was found that, in order to suppress soft in the welding heat affected zone
Change, contain on the basis of the content without V or control V and be used as solution strengthening element (solute strengthening
Element Si) is effective.On the other hand, the magnetic characteristic in highfield is caused to reduce because of containing for Si.Therefore, carry out
It is used for the research for improving magnetic characteristic, as a result specify that：Thick (coarse) cementite generation is suppressed to the limit, made and mother
Matching relationship (coherent relation) good Carbide Precipitation of material (matrix) is to take into account high intensity and good magnetic
The condition of characteristic.
The present invention is completed based on above-mentioned opinion, regard herein below as purport.
[1] a kind of magnetic pole hot rolled steel plate, wherein, composition composition contains C in terms of quality %：More than 0.02% and 0.12%
Below, Si：More than 0.1% and less than 0.7%, Mn：More than 0.8% and less than 1.6%, P：Less than 0.03%, S：0.005% with
Under, Al：Less than 0.08%, N：Less than 0.006%, Nb：More than 0.06% and less than 0.20%, surplus by Fe and inevitably
Impurity (incidental impurities) is constituted,
The ferritic phase of tissue is calculated as more than 98% with area occupation ratio, and the Fe of precipitation is 0.22 relative to Fe amounts contained in steel
Below quality %, the Nb separated out are more than 80 mass %, the carbide containing Nb separated out relative to Nb amounts contained in steel
Average grain diameter is below 6nm,
The yield strength of rolling direction (rolling direction) is more than 500MPa, magnetic flux density B50For 1.4T with
On, magnetic flux density B100For more than 1.5T, the minimum of the Vickers hardness of welding heat affected zone for (Vickers hardness of mother metal it is flat
Average -30) more than.
[2] magnetic pole hot rolled steel plate as described above described in [1], it is characterised in that further meet following formula (1).
Wherein, %C, %Nb, %V, %Ti represent the content of each element.In addition, being set as 0 when not containing.
[3] magnetic pole hot rolled steel plate as described above described in [1] or [2], wherein, on the basis of mentioned component composition, with
Quality % meters contain V：0.01% less than 0.05%, Ti：0.01% less than one or more of 0.05%.
[4] a kind of manufacture method of magnetic pole hot rolled steel plate, wherein, will have any one of above-mentioned [1]~[3]
The steel former material of composition composition is heated more than 1100 DEG C and at less than 1350 DEG C of temperature, then, is implemented more than 1100 DEG C
At a temperature of complete roughing (rough rolling) and by final rolling temperature (finishing rolling temperature) set
For more than 840 DEG C hot rollings, cooled down within after finish rolling terminates 3 seconds with more than 30 DEG C/sec of average cooling rate, so
Afterwards, batched (coil) more than 550 DEG C and at less than 700 DEG C of temperature.
[5] manufacture method of magnetic pole hot rolled steel plate as described above described in [4], it is characterised in that one is entered to surface of steel plate
Step implements plating.
[6] manufacture method of magnetic pole hot rolled steel plate as described above described in [5], it is characterised in that above-mentioned plating is
Galvanizing (hot-dip galvanizing) processing, alloyed zinc hot dip galvanized (hot-dip galvannealing) processing, plating
Any of zinc (electrogalvanized plating) processing.
[7] manufacture method of magnetic pole hot rolled steel plate as described above described in [5] or [6], it is characterised in that in above-mentioned plating
The composition of the coating formed in processing contains more than one or both of Zn, Si, Al, Ni, Mg.
[8] a kind of hydroelectric generation rim component, it is as the magnetic pole hot-rolled steel any one of above-mentioned [1]~[3]
Plate is constituted.
It should be noted that in the present invention, magnetic pole is with without the steel plate (hot rolling for implementing plating with hot rolled steel plate
Steel plate), implement the steel plate (GI) of galvanizing processing, further implement the steel plate of Alloying Treatment after galvanizing processing
(GA) any of steel plate (EG) of electrogalvanizing processing, is implemented as object.
Invention effect
According to the present invention it is possible to obtain weldability and excellent in magnetic characteristics of the yield strength of rolling direction for more than 500MPa
Magnetic pole hot rolled steel plate.The magnetic pole of the present invention is suitable for hydroelectric generation rim component etc. with hot rolled steel plate.By in waterpower
Using the magnetic pole hot rolled steel plate of the present invention in generating rim component, hydroelectric high efficiency and equipment longevity can be realized
The raising of life, its effect is notable.
Embodiment
Hereinafter, the present invention is described in detail.It should be noted that as long as no special declaration, following % is
Refer to quality %.
First, the tissue of the essential condition as steel plate of the present invention is illustrated.
The area occupation ratio of ferritic phase：More than 98% (including 100%)
During in the big state of dislocation density (dislocation density), magnetic flux density is significantly reduced.Therefore, need
Formed not comprising the bayesian body phase (bainite phase) containing a large amount of dislocation densities, martensitic phase (martensite
Phase the tissue of low-temperature phase as) covert (dislocation density).In the present invention, in order to meet desired magnetic
Characteristic, the area occupation ratio of ferritic phase is set as more than 98%.Surplus can enumerate bayesian body phase, martensitic phase and pearlite.
The Fe of precipitation is less than 0.22% relative to Fe amounts contained in steel
Cementite is derived from as the Fe of precipitate.Thick cementite causes magnetic flux density to reduce, it is therefore preferable that to the greatest extent may be used
It can reduce.The magnetic flux density required in the present invention is obtained to reduce cementite, it is necessary to by " the Fe amounts of precipitation " relative to " steel
In contained Fe amounts " ratio (below, otherwise referred to as Fe amount of precipitations) be set as less than 0.22%.Preferably 0.20% with
Under.It should be noted that Fe amount of precipitations can be measured according to the method described in embodiment described later.
In order to suppress cementite generation, preferably make containing C amounts separated out as much as possible in the form of the carbide containing Nb.
It is therefore preferable that meeting following (1) formulas.
Wherein, %C, %Nb, %V, %Ti represent the content of each element.In addition, being set as 0 when not containing.
Above-mentioned (1) formula be represent chemically make in the case that manufacturing condition is appropriate from the viewpoint of composition C and Nb, V and/
Or Ti is combined and separated out in the form of fine (fine) carbide so that the formula of cementite reduction, by being set as
Less than 0.040, the amount of precipitation of cementite is the scope that will not reduce magnetic flux density.Magnetic flux density B50For more than 1.5T, magnetic flux
Density B100For more than 1.6T particularly excellent magnetic characteristic by the way that (1) formula is set as into less than 0.03 obtains.On the other hand, C
Fine carbide is formed, therefore, (1) formula is preferably more than -0.005.
In addition, the C not combined with Nb, V and Ti is separated out in the form of Fe carbide.In order that the C almost all contained
Separated out in the form of the fine carbide containing Nb, V and Ti, the roughing before finish rolling is completed more than 1100 DEG C.
The Nb amounts of precipitation are more than 80 mass % relative to Nb amounts contained in steel
In the present invention, by make the fine carbide containing Nb disperse, can obtain yield strength for 500MPa with
On high intensity." the Nb amounts of precipitation " (sometimes, also referred to as Nb amount of precipitations or Nb are analysed relative to the ratio of " in steel contained Nb amounts "
Go out ratio) when being less than 80%, it is impossible to desired intensity is obtained, and then causes because of solid solution Nb influence magnetic flux density to reduce.From
Above-mentioned viewpoint is set out, and Nb amount of precipitations are set as more than 80%.Preferably more than 85%.It should be noted that Nb amount of precipitations can be with
It is measured according to the method described in embodiment described later.
The average grain diameter of the carbide containing Nb separated out is below 6nm
Raised by the intensive quantity for making the carbide containing Nb scattered and improving with the reduction of carbide particle diameter.In order to
Obtain high intensity that yield strength is more than 500MPa, it is necessary to the average grain diameter for making the carbide containing Nb of precipitation be 6nm with
Under.It should be noted that the average grain diameter of carbide can be measured according to the method described in embodiment described later.
Then, the restriction reason to the composition composition of the present invention is illustrated.
C：More than 0.02% and less than 0.12%
C is the member for the high intensity for forming the fine carbide containing Nb by being combined with Nb to contribute to steel plate
Element.In order to obtain more than 500MPa yield strength, it is necessary at least containing more than 0.02% C.Preferably more than 0.03%.Separately
On the one hand, containing more than 0.12% can generate cementite so that magnetic flux density is reduced.Therefore, C upper limit amount is set as
0.12%.Preferably less than 0.10%.
Si：More than 0.1% and less than 0.7%
Si is heat stable solution strengthening element, the effect with the softening for suppressing welding heat affected zone.In addition, Si has
Having makes cementite miniaturization, suppresses the dysgenic effect that magnetic flux density is reduced caused by cementite is separated out.So, Si exists
It is important condition in the present invention.The lower limit amount of Si for obtaining these effects is 0.1%.Preferably more than 0.2%, it is more excellent
Elect more than 0.35% as.On the other hand, when Si contents are more than 0.7%, it is bad that the magnetic flux density because caused by containing Si is reduced
Influence becomes notable, and produces red rust (red scale) in surface of steel plate, damages outward appearance, or plating reduction.Therefore,
Si upper limit amount is set as 0.7%.Preferably less than 0.6%.
Mn：More than 0.8% and less than 1.6%
Carbide containing Nb is with fine from austenite (austenite) to the low temperature of ferritic phase transition temperature
Change.Mn has reduction from austenite to the effect of ferritic phase transition temperature, therefore, by containing Mn, the carbide containing Nb
Miniaturization and high intensity.In order to obtain more than 500MPa yield strength, Mn needs to be set as more than 0.8%.On the other hand,
During more than 1.6%, easy bainite phase causes caused by thick cementite generation intensity decreases, magnetic flux density
Deviation.Therefore, the range set of Mn contents is more than 0.8% and less than 1.6%.Preferably more than 0.9% and less than 1.5%.
P：Less than 0.03%
P is that occur segregation in crystal boundary (grain boundary) and make it that the toughness (toughness) of weld part is significantly bad
The element of change.It is therefore preferable that reducing P as far as possible.In the present invention, in order to avoid above mentioned problem, P content is set as 0.03%
Below.Preferably less than 0.02%.
S：Less than 0.005%
S exists in steel in the form of the field trashes such as MnS (inclusion).The field trash is thick, therefore, causes magnetic flux
Density is reduced.Therefore, in the present invention, it is preferred to reduce S contents as far as possible, it is set as less than 0.005%.Preferably 0.003%
Below.
Al：Less than 0.08%
In the stage of steel-making when to contain Al in the form of deoxidier, contain more than 0.02%.On the other hand, Al content exceedes
When 0.08%, magnetic flux density reduction is caused because of the thick field trash such as aluminum oxide.Therefore, Al content be set as 0.08% with
Under.Preferably less than 0.07%.
N：Less than 0.006%
N is combined with Nb and is formed thick nitride, thus causes magnetic flux density to reduce.Further, since making to contribute to strong
The amount of precipitation for the fine carbide containing Nb changed is reduced, therefore also causes intensity decreases.It is therefore preferable that reducing N as far as possible
Content, 0.006% is set as by upper limit amount.Preferably less than 0.005%.
Nb：More than 0.06% and less than 0.20%
Nb is the element for the high intensity to form fine carbide and contribute to steel plate.In order to obtain more than 500MPa's
Yield strength is, it is necessary to contain more than 0.06% Nb amounts.When on the other hand, more than 0.20%, during heating of plate blank before hot rolling,
To the contribution saturation of high intensity, and magnetic flux density can not be caused to reduce the thick carbide dissolution containing Nb.Cause
This, is more than 0.06% and less than 0.20% by the range set of Nb contents.Preferably more than 0.08% and less than 0.18%.With
In the rolling direction for obtaining more than 550MPa yield strength preferred scope be more than 0.10% and less than 0.18%.
Surplus is Fe and inevitable impurity.
It is above the composition composition in the present invention, on the basis of mentioned component composition, one can be entered according to following purposes
Step contains V：0.01% less than 0.05%, Ti：0.01% less than one or more of 0.05%.
V and Ti are to be combined with C and contribute to the element of further high intensity.In order to obtain the effect, preferably V and Ti
Contain more than 0.01%.When on the other hand, containing more than 0.05% V, the carbide containing V in welding heat affected zone
The influence of the caused softening of dissolving becomes notable, weldability reduction.During containing more than 0.05% Ti, the slab before hot rolling
The thick carbide containing Ti is remained in heating process, causes magnetic flux density to reduce.Therefore, containing sometimes, it is set as V：
0.01% less than 0.05%, Ti：0.01% less than 0.05%.Preferably V：More than 0.01% and 0.04% with
Under, Ti：More than 0.01% and less than 0.03%.
Then, the magnetic pole of the present invention is illustrated with the restriction reason of the characteristic of hot rolled steel plate.
The yield strength of rolling direction is more than 500MPa
In the case of for hydroelectric generation rim component etc., it is desirable to intensity.The yield strength of rolling direction is
During more than 500MPa, thickness of slab can be reduced and efficient hydroelectric generation rim component is applied to.In this case, based on
The yield strength of the tension test in the parallel direction of rolling direction becomes important, therefore, and the yield strength to rolling direction is carried out
Regulation.It is particularly suitable for steel plate of the yield strength less than 700MPa of the present invention.
Magnetic flux density B50For more than 1.4T, magnetic flux density B100For more than 1.5T
Magnetic flux density B50For more than 1.4T, magnetic flux density B100During for more than 1.5T, for hydroelectric generation rim component
In the case of, hydroelectric high efficiency can be realized.
The minimum of the Vickers hardness of welding heat affected zone is more than (average value -30 of the Vickers hardness of mother metal)
Hydroelectric generation is engaged by welding mostly with rim component.By the way that the Vickers hardness of welding heat affected zone is set
More than (average value -30 of the Vickers hardness of mother metal), the defect, bad of weld part can be suppressed.Welding condition now with
Condition described in embodiment is equal.
Then, the magnetic pole of the present invention is illustrated with the manufacture method of hot rolled steel plate.
The magnetic pole of the present invention can be manufactured by the following method with hot rolled steel plate：Steel former material (the steel that mentioned component is constituted
Base) more than 1100 DEG C and less than 1350 DEG C are heated, then, roughing and general are completed at a temperature of implementing more than 1100 DEG C
Final rolling temperature is set as more than 840 DEG C of hot rolling, with more than 30 DEG C/sec of average cooling rate within after finish rolling terminates 3 seconds
Cooling, then, more than 550 DEG C and less than 700 DEG C are batched.
In the present invention, the method for smelting of steel is not particularly limited, can be using public affairs such as converter (converter), electric furnaces
The method of smelting known.Furthermore it is possible to carry out double refining using vacuum degassing furnace (vacuum degassing furnace)
(secondary refining).Then, from productivity ratio, quality the problem of, considers, slab (steel preferably is made by continuous metal cast process
Former material), but it is also possible to pass through ingot casting-split rolling method method (ingot casting and blooming), sheet blank continuous casting method etc.
Slab is made in known casting method.
The heating-up temperature of steel former material：More than 1100 DEG C and less than 1350 DEG C
, it is necessary to steel former material be heated and formed the austenite phase of substantial homogeneous before hot rolling.Heating-up temperature is low
When 1100 DEG C, it is impossible to by the thick carbide dissolution containing Nb and Ti, intensity and magnetic flux density reduction.On the other hand, plus
When hot temperature is more than 1350 DEG C, oxide skin (scale) growing amount increases, and oxide skin, the surface of hot rolled steel plate are bitten in hot rolling
Character is deteriorated.Therefore, the heating-up temperature of steel former material is set as more than 1100 DEG C and less than 1350 DEG C.Preferably more than 1150 DEG C and
Less than 1300 DEG C.But, when implementing hot rolling to steel former material, the steel former material after casting is in more than 1100 DEG C and less than 1350 DEG C
In the case of temperature range or steel former material carbide dissolve in the case of, direct sending rolling can be carried out without former to steel
Material is heated.
Roughing is completed at a temperature of more than 1100 DEG C and final rolling temperature is set as to more than 840 DEG C of hot rolling
The C not combined with Nb, V and Ti is separated out in the form of Fe carbide.In order that the C almost all contained with containing
The form of Nb, V and Ti fine carbide is separated out, it is necessary to make the roughing before finish rolling be completed more than 1100 DEG C.Because,
Less than 1100 DEG C complete roughing in the case of, the strain imported using in roughing as driving force, therefore after keep for a long time and
Separate out the carbide containing Nb, V and Ti thickly in austenite, this causes the harmful effect for intensity and magnetic flux density to become
Obtain significantly.When final rolling temperature is less than 840 DEG C, starts ferrite transformation in finish rolling and form the tissue that ferrite crystal grain stretches.
A large amount of dislocations are imported with the inside of the ferrite crystal grain of the stretching, extension, therefore, cause magnetic flux density to reduce.Therefore, final rolling temperature
It is set as more than 840 DEG C.Preferably more than 860 DEG C.It should be noted that the temperature in finish rolling is less than 1100 DEG C, but in finish rolling
Tandem rolling compared with roughing, the time do not separate out, grown, therefore, harmful effect during above-mentioned roughing is not notable.
Cooled down within after finish rolling terminates 3 seconds with more than 30 DEG C/sec of average cooling rate
Carbide containing Nb is with from austenite to the low temperature of ferritic phase transition temperature and miniaturization.In order to obtain
Average grain diameter is below 6nm carbide, it is necessary to will be set as less than 700 DEG C from austenite to ferritic phase transition temperature.For
This within after finish rolling terminates 3 seconds with more than 30 DEG C/sec of average cooling rate, it is necessary to be cooled down.It should be noted that flat
Equal cooling velocity is the average cooling rate from final rolling temperature to 700 DEG C.
Coiling temperature：More than 550 DEG C and less than 700 DEG C
When coiling temperature is more than 700 DEG C, carbide coarsening, it is impossible to obtain desired intensity and magnetic characteristic.On the other hand,
During less than 550 DEG C, thus bainite phase reduces magnetic characteristic.Therefore, by the range set of coiling temperature be 550 DEG C with
Go up and less than 700 DEG C.Preferably more than 580 DEG C and less than 680 DEG C.
The magnetic pole hot rolled steel plate of the present invention is manufactured by the above method.Even if it should be noted that by the present invention magnetic
Pole carries out logical plate with hot rolled steel plate in annealing temperature is less than 720 DEG C of continuous hot-dipping production line, to material also without shadow
Ring.It therefore, it can that surface of steel plate is further implemented plating and has coating in surface of steel plate.In addition, plating, plating
The composition of bath will not also bring influence to material, therefore, as plating, can apply galvanizing processing, alloyed hot-dip
Zinc processing, electrogalvanizing processing in any one.In addition, as the composition of plating bath, as long as containing in Zn, Si, Al, Ni, Mg
One or more.That is, the composition of the coating formed in plating can be containing in Zn, Si, Al, Ni, Mg
It is one or more kinds of.
The magnetic pole of the invention obtained by the above method is suitable for the part of the high magnetic pole of requirement with hot rolled steel plate, particularly
It is best suited for the use as hydroelectric generation rim component.For example, by the hot rolled steel plate of the present invention by shearing, being punched, swash
The methods such as light cutting are cut into defined shape, are laminated, can be used as the electromagnetism towards wheel rim, iron core (pole core etc.)
Component is used.Particularly, hot rolled steel plate of the invention can be suitable for needing to take into account high intensity and the hair of good magnetic characteristic
Motor wheel rim.In the stacking of steel plate, preferred pair steel plate implements insulating wrapped or sandwiched insulation raw material etc. make between steel plate
It is electrically insulated between the steel plate and steel plate of stacking.
Embodiment 1
For the steel former material of the wall thickness 250mm with the composition composition shown in table 1, made under the hot-rolled condition shown in table 2
Fabricate-heat rolled steel plate.For a part of hot rolled steel plate, further implement alloyed zinc hot dip galvanized processing.Alloyed zinc hot dip galvanized processing passes through
Annealing temperature is less than 700 DEG C, the composition of plating bath (molten bath) is that Zn-0.13 mass %Al, the temperature of plating bath are 460
DEG C, alloying temperature manufactured for 530 DEG C of continuous hot-dipping production line, coating adhesion amount (coating weight) is set
For every 45~65g/m of one side2。
Cut from the thickness of slab 1.6mm~3.2mm obtained by the above method hot rolled steel plate or alloyed hot-dip galvanized steel sheet
Test film, is observed tissue by following methods, evaluates performance.
(i) structure observation
The area occupation ratio of each phase is evaluated by following methods.From hot rolled steel plate or alloyed hot-dip galvanized steel sheet, according to
The parallel section of rolling direction is cut for the mode of sightingpiston, is corroded using 3% nital (nital)
(etching) metal structure of thickness of slab central part is shown, 400 times are amplified to using sweep type light microscope, to 10
The visual field is shot.Ferritic phase is that have not observing corrosion trace, the tissue of the form of cementite in crystal grain.Pass through image
Bayesian body phase, martensitic phase, pearlite (pearlite) beyond ferritic phase etc. are isolated them in parsing, using relative to
The area occupation ratio of field of view carries out asking calculation.When seeking calculation area, a part for ferrite grain boundaries as ferritic phase is counted.
On the average grain diameter of the carbide containing Nb of precipitation, using transmission electron microscope with more than 135000 times
Observed, take the particle diameter of more than 100 points of carbide to be averaged, obtain equivalent circle diameter as the particle diameter of each carbide.
On Fe amount of precipitations, in 10%AA systems electrolyte (the quality % tetramethyl ammonium chlorides of 10 volume % acetylacetone,2,4-pentanediones-1-first
Alcohol) in, will about 0.2g with 20mA/cm2Current density carry out constant-current electrolysis after, by filter from electrolyte trap separate out
Thing, Fe amounts contained in precipitate are obtained using ICP-MS methods, the base steel after obtaining and being electrolysed by constant-current electrolysis
The ratio of quality, thus obtains Fe amount of precipitations.
On Nb amount of precipitations (Nb separates out ratio), constant current is carried out by the step same with the assay method of Fe amount of precipitations
Electrolysis, Nb amounts contained in electrolyte are determined using ICP-MS methods.Contained Nb amounts are in solid solution condition in the electrolyte
Nb amounts, Nb amount of precipitations are obtained by subtracting the Nb amounts in solid solution condition from Nb contents.
(ii) tension test
From hot rolled steel plate or alloyed hot-dip galvanized steel sheet, No. 5 drawings of JIS are made along the direction parallel relative to rolling direction
Stretch test film, carry out 5 defined tension tests according to JIS Z 2241 (2011), obtain average yield strength (YS),
Tensile strength (TS), percentage of total elongation (El).The crosshead speed set of tension test is 10mm/ minutes.
(iii) magnetic flux density is determined
30mm × 280mm sample is cut from hot rolled steel plate or alloyed hot-dip galvanized steel sheet, is determined using DC Magnetic Properties
Device, magnetic flux density B is obtained by the measure according to JIS C 255550With magnetic flux density B100。B50And B100Magnetization is represented respectively
Magnetic flux density under power 5000A/m and 10000A/m.
(iv) weldability evaluation
As soldering test, progress is evaluated using the CO2 welding of diameter 1.2mm wire.Welding
Condition be speed of welding be 80cm/ minutes, welding current be that 220A, weldingvoltage are 25V, plate gap (gap) 1mm butt welding.
After welding, welding seam part section is cut out, the thickness of slab central portion of its section is entered with 0.5mm intervals relative to the direction for crossing weld part
Row test load is 0.49N Vickers hardness test.On the other hand, the hardness of mother metal is set as the test load pair with 0.49N
Average value obtained from 5 points of the position finding apart from more than weld part 30mm.Shown in table 3 mother metal hardness (mother metal hardness
Average value) and minimum hardness (welding heat affected zone hardness minimum) in heat affected area difference.
The result obtained as described above is shown in Table 3.
Understand：The yield strength YS that example of the present invention has obtained rolling direction is more than 500MPa and welding heat affected
The minimum of the Vickers hardness in area is the weldability and magnetic flux density B more than (average value -30 of the Vickers hardness of mother metal)50
For more than 1.4T, magnetic flux density B100For the hot rolled steel plate (alloyed hot-dip galvanized steel sheet) of more than 1.5T excellent in magnetic characteristics.It is another
In aspect, the comparative example for deviateing the scope of the present invention, certain more than one of yield strength, weldability, magnetic characteristic is poor.
Claims (8)
1. a kind of magnetic pole hot rolled steel plate, wherein, composition composition contains C in terms of quality %：More than 0.02% and less than 0.12%,
Si：More than 0.1% and less than 0.7%, Mn：More than 0.8% and less than 1.6%, P：Less than 0.03%, S：Less than 0.005%,
Al：Less than 0.08%, N：Less than 0.006%, Nb：More than 0.06% and less than 0.20%, surplus by Fe and inevitably it is miscellaneous
Texture into,
The ferritic phase of tissue is calculated as more than 98% with area occupation ratio,
The Fe of precipitation is below 0.22 mass % relative to Fe amounts contained in steel, the Nb of precipitation is relative to Nb amounts contained in steel
Average grain diameter for more than 80 mass %, the carbide containing Nb separated out is below 6nm,
The yield strength of rolling direction is more than 500MPa, magnetic flux density B50For more than 1.4T, magnetic flux density B100For 1.5T with
On, the minimum of the Vickers hardness of welding heat affected zone is more than (average value -30 of the Vickers hardness of mother metal).
2. magnetic pole hot rolled steel plate as claimed in claim 1, it is characterised in that further meet following formula (1),
Wherein, %C, %Nb, %V, %Ti represent the content of each element, in addition, being set as 0 when not containing.
3. magnetic pole hot rolled steel plate as claimed in claim 1 or 2, wherein, on the basis of composition composition, with quality %
Meter contains V：0.01% less than 0.05%, Ti：0.01% less than one or more of 0.05%.
4. a kind of manufacture method of magnetic pole hot rolled steel plate, wherein, there will be composition according to any one of claims 1 to 3
The steel former material of composition is heated more than 1100 DEG C and at less than 1350 DEG C of temperature, then, implements the temperature more than 1100 DEG C
The lower hot rolling for completing roughing and final rolling temperature being set as to more than 840 DEG C, with more than 30 DEG C/sec within after finish rolling terminates 3 seconds
Average cooling rate cooled down, then, batched more than 550 DEG C and at less than 700 DEG C of temperature.
5. the manufacture method of magnetic pole hot rolled steel plate as claimed in claim 4, it is characterised in that to the further reality of surface of steel plate
Apply plating.
6. the manufacture method of magnetic pole hot rolled steel plate as claimed in claim 5, it is characterised in that the plating is hot dip
Any of zinc processing, alloyed zinc hot dip galvanized processing, electrogalvanizing processing.
7. the manufacture method of the magnetic pole hot rolled steel plate as described in claim 5 or 6, it is characterised in that in the plating
The composition of the coating of middle formation contains more than one or both of Zn, Si, Al, Ni, Mg.
8. a kind of hydroelectric generation rim component, it is by magnetic pole according to any one of claims 1 to 3 hot rolled steel plate structure
Into.
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| JP2014-246562 | 2014-12-05 | ||
| JP2014246562 | 2014-12-05 | ||
| PCT/JP2015/005806 WO2016088321A1 (en) | 2014-12-05 | 2015-11-20 | Hot-rolled steel sheet for magnetic pole and method for manufacturing same, and rim member for hydroelectric power generation |
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| KR (1) | KR101966313B1 (en) |
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| CN115198187A (en) * | 2022-07-08 | 2022-10-18 | 山西太钢不锈钢股份有限公司 | 400 MPa-level hot-rolled magnetic pole steel and manufacturing method and application thereof |
| CN115244201A (en) * | 2020-05-08 | 2022-10-25 | 日本制铁株式会社 | Hot-rolled steel sheet and method for producing same |
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| WO2014148001A1 (en) * | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
| CN104080938A (en) * | 2012-01-31 | 2014-10-01 | 杰富意钢铁株式会社 | Hot-rolled steel for power generator rim and method for manufacturing same |
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| JPS63166931A (en) | 1986-12-27 | 1988-07-11 | Nippon Steel Corp | Manufacture of high tension hot rolled steel sheet having high magnetic flux density |
| JP4273768B2 (en) | 2001-12-28 | 2009-06-03 | Ｊｆｅスチール株式会社 | Hot-rolled steel sheet for iron core of rotating machine and manufacturing method thereof |
| CN103451532A (en) * | 2013-09-12 | 2013-12-18 | 武汉钢铁(集团)公司 | Hot-rolled magnetic yoke steel with yield strength not less than 750Mpa and production method thereof |
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2015
- 2015-11-20 KR KR1020177013924A patent/KR101966313B1/en active IP Right Grant
- 2015-11-20 MX MX2017007019A patent/MX2017007019A/en unknown
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|---|---|---|---|---|
| CN104080938A (en) * | 2012-01-31 | 2014-10-01 | 杰富意钢铁株式会社 | Hot-rolled steel for power generator rim and method for manufacturing same |
| WO2014148001A1 (en) * | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
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| CN115244201A (en) * | 2020-05-08 | 2022-10-25 | 日本制铁株式会社 | Hot-rolled steel sheet and method for producing same |
| CN115244201B (en) * | 2020-05-08 | 2023-05-12 | 日本制铁株式会社 | Hot-rolled steel sheet and method for producing same |
| CN115198187A (en) * | 2022-07-08 | 2022-10-18 | 山西太钢不锈钢股份有限公司 | 400 MPa-level hot-rolled magnetic pole steel and manufacturing method and application thereof |
| CN115198187B (en) * | 2022-07-08 | 2024-04-26 | 山西太钢不锈钢股份有限公司 | 400 MPa-grade hot-rolled magnetic pole steel and manufacturing method and application thereof |
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| JP6020769B1 (en) | 2016-11-02 |
| WO2016088321A1 (en) | 2016-06-09 |
| CN107002196B (en) | 2019-01-01 |
| JPWO2016088321A1 (en) | 2017-04-27 |
| KR20170072312A (en) | 2017-06-26 |
| KR101966313B1 (en) | 2019-04-05 |
| MX2017007019A (en) | 2017-08-14 |
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