CN107002196B - Magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component - Google Patents
Magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component Download PDFInfo
- Publication number
- CN107002196B CN107002196B CN201580065641.8A CN201580065641A CN107002196B CN 107002196 B CN107002196 B CN 107002196B CN 201580065641 A CN201580065641 A CN 201580065641A CN 107002196 B CN107002196 B CN 107002196B
- Authority
- CN
- China
- Prior art keywords
- less
- steel plate
- rolled steel
- hot rolled
- magnetic pole
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 93
- 239000010959 steel Substances 0.000 title claims abstract description 93
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 230000004907 flux Effects 0.000 claims abstract description 37
- 238000005096 rolling process Methods 0.000 claims abstract description 37
- 239000000463 material Substances 0.000 claims abstract description 26
- 238000001556 precipitation Methods 0.000 claims abstract description 23
- 238000003466 welding Methods 0.000 claims abstract description 21
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 13
- 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
- 238000007747 plating Methods 0.000 claims description 18
- 229910052719 titanium Inorganic materials 0.000 claims description 17
- 238000012545 processing Methods 0.000 claims description 15
- 229910052720 vanadium Inorganic materials 0.000 claims description 12
- 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
- 239000000203 mixture Substances 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
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 229910052749 magnesium Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 239000004615 ingredient Substances 0.000 claims description 2
- 230000015572 biosynthetic process Effects 0.000 claims 1
- 239000012535 impurity Substances 0.000 abstract description 4
- 238000000034 method Methods 0.000 description 22
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 21
- 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
- 230000000694 effects Effects 0.000 description 9
- 238000012360 testing method Methods 0.000 description 9
- 230000002829 reductive effect Effects 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 229910001563 bainite Inorganic materials 0.000 description 6
- 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
- 238000010438 heat treatment 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
- 238000004090 dissolution Methods 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
- 239000002244 precipitate Substances 0.000 description 4
- 230000009467 reduction Effects 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000005868 electrolysis reaction Methods 0.000 description 3
- 230000036961 partial effect Effects 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 239000006104 solid solution Substances 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
- 230000002411 adverse Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000004458 analytical method 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
- 230000006866 deterioration Effects 0.000 description 2
- 238000007598 dipping method Methods 0.000 description 2
- 238000001095 inductively coupled plasma mass spectrometry Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000010813 municipal solid waste Substances 0.000 description 2
- 238000010248 power generation Methods 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 compound [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
- 230000005540 biological transmission Effects 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 238000003763 carbonization Methods 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
- 238000005530 etching 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
- 230000005415 magnetization Effects 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
- 238000000399 optical microscopy Methods 0.000 description 1
- 239000002245 particle Substances 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
- 229920006395 saturated elastomer Polymers 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (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 high-intensitive and magnetic pole of weldability and excellent in magnetic characteristics hot rolled steel plate and its manufacturing method, hydroelectric generation rim component.Containing C:0.02% or more and 0.12% or less, Si:0.1% or more and 0.7% or less, Mn:0.8% or more and 1.6% or less, P:0.03% or less, S:0.005% or less, Al:0.08% or less, N:0.006% or less, Nb:0.06% or more and 0.20% hereinafter, surplus is made of Fe and inevitable impurity.Ferritic phase is calculated as 98% or more with the area ratio, the Fe of precipitation is 0.22 mass % or less relative to Fe amount contained in steel, the Nb of precipitation is 80 mass % or more relative to Nb amount contained in steel, the average grain diameter for the carbide containing Nb being precipitated is 6nm or less, the yield strength of rolling direction is 500MPa or more, magnetic flux density B50For 1.4T or more, magnetic flux density B100For 1.5T or more, the minimum of the Vickers hardness of welding heat affected zone is (average value -30 of the Vickers hardness of base material) or more.
Description
Technical field
The present invention relates to the magnetic pole hot rolled steel plate for being suitable for hydroelectric generation rim component etc. and its manufacturing method and
Hydroelectric generation rim component.
Background technique
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
The needs of the natural energy resources of body increase.In addition, from the viewpoint of inhibiting such global warming, recently as clean energy resource
Hydroelectric generation be considered as wishing.The generators such as hydroelectric generator have 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 power generation capacity, need to revolve rotor high speed
Turn.Therefore, wheel rim is required to keep high-intensitive in order to bear high-speed rotating centrifugal force.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
It is easy to change, therefore, also requires weldability (weldability) excellent.
Above-mentioned requirements are answered, up to the present, for the hot rolled steel plate for being conceived to magnetic characteristic, weldability, propose various technologies.
For example, in patent document 1, by having the ferritic phase (ferrite for being 95% or more comprising the area ratio
Phase it) and in the crystal grain of the ferritic phase (crystal grain) 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 more than and less than 10 μ
In the range of m, the available yield strength with rolling direction is the intensity and magnetic flux density B of 700MPa or more50For 1.5T
Above, B100For the steel plate of the electromagnetic property of 1.6T or more.
In patent document 2, will be contained in terms of weight % C:0.05~0.15%, Si:0.5% or less, Mn:0.70~
2.00%, it is batched after the steel plate progress hot rolling of Ti:0.10~0.30%, B:0.0015~0.0050% at 500 DEG C or less,
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,
In, containing C≤0.10%, Ti:0.02~0.2%, further contain at least one of Mo≤0.7%, W≤1.5%, essence
On be dispersed in ferritic structure containing Ti, with the carbide less than 10nm of at least one of Mo and W, with 590MPa
Grade or more intensity.
Existing technical literature
Patent document
Patent document 1: International Publication No. 2013/115205
Patent document 2: Japanese Unexamined Patent Application 63-166931 bulletin
Patent document 3: Japanese Unexamined Patent Publication 2003-268509 bulletin
Summary of the invention
Problem to be solved by the invention
But in the technology proposed in patent document 1, due to containing solid solution V (solute V), analyse coarsely
The control of cementite (cementite) amount out is extremely difficult, and then weldability deteriorates.
In the technology proposed in patent document 2, need in coiling temperature to be 500 DEG C of uncontrollable temperature models below
Enclose it is interior batched, between coiled material and coiled material in characteristic deviation become problem.In addition, low temperature phase change phase factor phase transition strain is not
Uniformly caused by plate shape deterioration and be not suitable as wheel rim component.
It in the technology proposed in patent document 3, is not accounted for not only for weldability, and for coarse cementite
Influence do not account for yet, it is thus impossible to obtain stable magnetic characteristic.
In view of the foregoing, it is 500MPa or more the purpose of the present invention is to provide the yield strength of rolling direction and welds
The magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component of property and excellent in magnetic characteristics.
The method for solving problem
For high intensity and the condition of steel plate that has both good weldability and good magnetic characteristic has made intensive studies,
As a result, it has been found that the hardness in welding heat affected zone (heat-affected zone) reduces the carbonization containing V big by solubility
It is affected brought by the dissolution (re-solution) of object.And it was found that in order to inhibit soft in the welding heat affected zone
Change, containing as solution strengthening element (solute strengthening on the basis of not adding V or controlling the content of V
Element Si) is effective.On the other hand, the magnetic characteristic in highfield is reduced.Therefore, it carries out
For improving the research of magnetic characteristic, as a result specify: coarse (coarse) cementite is generated inhibit to the limit, make with it is female
Matching relationship (coherent relation) good Carbide Precipitation of material (matrix) is to take into account high-intensitive and good magnetic
The condition of characteristic.
The present invention is completed based on above-mentioned opinion, using the following contents as purport.
[1] a kind of magnetic pole hot rolled steel plate, wherein contain C:0.02% or more and 0.12% at being grouped as in terms of quality %
Below, Si:0.1% or more and 0.7% or less, Mn:0.8% or more and 1.6% or less, P:0.03% or less, S:0.005% with
Under, Al:0.08% or less, N:0.006% or less, Nb:0.06% or more and 0.20% or less, surplus be by Fe and inevitably
Impurity (incidental impurities) is constituted,
The ferritic phase of tissue is calculated as 98% or more with the area ratio, and the Fe of precipitation is 0.22 relative to Fe amount contained in steel
Quality % or less, the Nb being precipitated are the carbide containing Nb of 80 mass % or more, precipitation relative to Nb amount contained in steel
Average grain diameter be 6nm hereinafter,
The yield strength of rolling direction (rolling direction) is 500MPa or more, magnetic flux density B50For 1.4T with
On, magnetic flux density B100For 1.5T or more, the minimum of the Vickers hardness of welding heat affected zone be (Vickers hardness of base material it is flat
Mean value -30) more than.
[2] the magnetic pole hot rolled steel plate as described in above-mentioned [1], which is characterized in that further satisfaction following formula (1).
Wherein, %C, %Nb, %V, %Ti indicate the content of each element.In addition, being set as 0 when not containing.
[3] the magnetic pole hot rolled steel plate as described in above-mentioned [1] or [2], wherein on the basis of mentioned component composition, with
Quality % meter is containing V:0.01% more than or lower than 0.05%, Ti:0.01% more than or lower than one or more of 0.05%.
[4] a kind of manufacturing method of magnetic pole hot rolled steel plate, wherein will have described in any one of above-mentioned [1]~[3]
It heats under 1100 DEG C or more and 1350 DEG C of temperature below at the steel former material being grouped as, then, implements at 1100 DEG C or more
At a temperature of complete roughing (rough rolling) and by final rolling temperature (finishing rolling temperature) set
For 840 DEG C or more of hot rolling, cooled down after finish rolling within 3 seconds with 30 DEG C/sec or more of average cooling rate, so
Afterwards, (coil) is batched under 550 DEG C or more and 700 DEG C of temperature below.
[5] manufacturing method of the magnetic pole hot rolled steel plate as described in above-mentioned [4], which is characterized in that surface of steel plate into one
Step implements plating.
[6] manufacturing method of the magnetic pole hot rolled steel plate as described in above-mentioned [5], which is characterized in that above-mentioned plating is
Hot galvanizing (hot-dip galvanizing) processing, alloyed zinc hot dip galvanized (hot-dip galvannealing) processing, plating
Any one of zinc (electrogalvanized plating) processing.
[7] manufacturing method of the magnetic pole hot rolled steel plate as described in above-mentioned [5] or [6], which is characterized in that in above-mentioned plating
The composition of the coating formed in processing contains one or more of Zn, Si, Al, Ni, Mg.
[8] a kind of hydroelectric generation rim component, the magnetic pole hot-rolled steel as described in any one of above-mentioned [1]~[3]
Plate is constituted.
It should be noted that in the present invention, magnetic pole is with no steel plate (hot rolling for implementing plating with hot rolled steel plate
Steel plate), the steel plate (GI) that implements hot galvanizing processing, after hot galvanizing processing further implement the steel plate of Alloying Treatment
(GA), any one of steel plate (EG) of electrogalvanizing processing is implemented as object.
Invention effect
According to the present invention it is possible to weldability and excellent in magnetic characteristics that the yield strength for obtaining rolling direction is 500MPa or more
Magnetic pole hot rolled steel plate.Magnetic pole of the invention is suitable for hydroelectric generation rim component etc. with hot rolled steel plate.By in waterpower
Magnetic pole hot rolled steel plate of the invention is used in power generation rim component, can be realized hydroelectric high efficiency and equipment longevity
The raising of life, significant effect.
Specific embodiment
Hereinafter, being described in detail to the present invention.It should be noted that as long as no special declaration, % below is
Refer to quality %.
Firstly, being illustrated to the tissue of the essential condition as steel plate of the present invention.
The area ratio of ferritic phase: 98% or more (including 100%)
When in the big state of dislocation density (dislocation density), magnetic flux density is significantly reduced.Therefore, it needs
It is formed and does not include the bainite 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
The area ratio of characteristic, ferritic phase is set as 98% or more.Surplus can enumerate bainite phase, martensitic phase and pearlite.
The Fe of precipitation is 0.22% or less relative to Fe amount contained in steel
Fe as precipitate derives from cementite.Coarse cementite causes magnetic flux density to reduce, it is therefore preferable that the greatest extent may be used
It can be reduced.The magnetic flux density required in the present invention is obtained to reduce cementite, is needed " the Fe amount of precipitation " relative to " steel
Contained in Fe amount " ratio (hereinafter, otherwise referred to as Fe amount of precipitation) be set as 0.22% or less.Preferably 0.20% with
Under.It should be noted that Fe amount of precipitation can be measured according to the method recorded in aftermentioned embodiment.
In order to inhibit cementite to generate, preferably make containing C amount be precipitated 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 indicate the content of each element.In addition, being set as 0 when not containing.
Above-mentioned (1) formula be indicate to make from the viewpoint of the chemically ingredient in manufacturing condition situation appropriate C and Nb, V and/
Or Ti is in conjunction with and by be precipitated the formula so that cementite reduction in the form of fine (fine) carbide, by being set as
0.040 hereinafter, the amount of precipitation of cementite is the range that magnetic flux density will not be made to reduce.Magnetic flux density B50For 1.5T or more, magnetic flux
Density B100It is obtained for the particularly excellent magnetic characteristic of 1.6T or more by the way that (1) formula is set as 0.03 or less.On the other hand, C
Fine carbide is formed, therefore, (1) formula is preferably -0.005 or more.
In addition, the C not in conjunction with Nb, V and Ti is precipitated in the form of Fe carbide.In order to make containing C almost all
It is precipitated in the form of the fine carbide containing Nb, V and Ti, the roughing before preferably making finish rolling is completed at 1100 DEG C or more.
The Nb amount of precipitation is 80 mass % or more relative to Nb amount contained in steel
In the present invention, by dispersing the fine carbide containing Nb, available yield strength be 500MPa with
On high intensity." the Nb amount of precipitation " relative to " Nb amount contained in steel " ratio (sometimes, also referred to as Nb amount of precipitation or Nb analysis
Ratio out) when being lower than 80%, desired intensity cannot be obtained, and then the influence because being dissolved Nb due to, reduces magnetic flux density.From
Above-mentioned viewpoint is set out, and Nb amount of precipitation is set as 80% or more.Preferably 85% or more.It should be noted that Nb amount of precipitation can be with
It is measured according to the method recorded in aftermentioned embodiment.
The average grain diameter for the carbide containing Nb being precipitated is 6nm or less
The intensive quantity improved and dispersing the carbide containing Nb is increased with the reduction of carbide partial size.In order to
Obtain the high intensity that yield strength is 500MPa or more, need to make the average grain diameter 6nm for the carbide containing Nb being precipitated with
Under.It should be noted that the average grain diameter of carbide can be measured according to the method recorded in aftermentioned embodiment.
Then, it is illustrated to of the invention at the restriction reason being grouped as.
0.12% or less C:0.02% or more and
C is that the fine carbide containing Nb is formed and in conjunction with Nb to facilitate the member of the high intensity of steel plate
Element.The yield strength of 500MPa or more in order to obtain needs at least C containing 0.02% or more.Preferably 0.03% or more.Separately
On the one hand, containing more than 0.12% can be such that cementite generates, so that magnetic flux density reduces.Therefore, the upper limit amount of C is set as
0.12%.Preferably 0.10% or less.
0.7% or less Si:0.1% or more and
Si is heat stable solution strengthening element, has the effect of inhibiting the softening of welding heat affected zone.In addition, Si has
There is the dysgenic effect for making cementite miniaturization, magnetic flux density caused by being precipitated because of cementite being inhibited to reduce.In this way, Si exists
Condition is important in the present invention.The lower limit amount of Si for obtaining these effects is 0.1%.Preferably 0.2% or more, it is more excellent
It is selected as 0.35% or more.On the other hand, when Si content is more than 0.7%, magnetic flux density is reduced bad because caused by containing Si
Influence becomes significantly, and generates red rust (red scale) in surface of steel plate, and damaging appearance or plating reduces.Therefore,
The upper limit amount of Si is set as 0.7%.Preferably 0.6% or less.
1.6% or less Mn:0.8% or more and
Carbide containing Nb is with fine from austenite (austenite) to the low temperature of ferritic phase transition temperature
Change.Mn have the effect of reduce from austenite to ferritic phase transition temperature, therefore, by containing Mn, the carbide containing Nb
It miniaturize and high intensity.The yield strength of 500MPa or more in order to obtain, Mn need to be set as 0.8% or more.On the other hand,
When more than 1.6%, it is easy bainite phase, leads to strength reduction caused by generating because of coarse cementite, magnetic flux density
Deviation.Therefore, the range of Mn content is set as 0.8% or more and 1.6% or less.Preferably 0.9% or more and 1.5% or less.
P:0.03% or less
P is that segregation occurs at crystal boundary (grain boundary) and makes the toughness (toughness) of weld part significant bad
The element of change.It is therefore preferable that reducing P as far as possible.In the present invention, in order to avoid the above problem, P content is set as 0.03%
Below.Preferably 0.02% or less.
S:0.005% or less
S exists in steel in the form of the field trashes such as MnS (inclusion).The field trash is coarse, therefore, causes magnetic flux close
Degree reduces.Therefore, in the present invention, it is preferred to reduce S content as far as possible, it is set as 0.005% or less.Preferably 0.003% or less.
Al:0.08% or less
When containing Al in the form of deoxidier in the stage of steel-making, contain 0.02% or more.On the other hand, Al content is more than
When 0.08%, because of the coarse field trash such as aluminium oxide magnetic flux density is reduced.Therefore, Al content be set as 0.08% with
Under.Preferably 0.07% or less.
N:0.006% or less
N forms coarse nitride in conjunction with Nb, thus magnetic flux density is caused to reduce.Further, since making to facilitate strong
The amount of precipitation for the fine carbide containing Nb changed is reduced, therefore also leads to strength reduction.It is therefore preferable that reducing N as far as possible
Upper limit amount is set as 0.006% by content.Preferably 0.005% or less.
0.20% or less Nb:0.06% or more and
Nb is the element for the high intensity to form fine carbide and facilitate steel plate.In order to obtain 500MPa or more
Yield strength needs the Nb amount containing 0.06% or more.When on the other hand, more than 0.20%, when heating of plate blank before hot rolling,
The coarse carbide dissolution containing Nb cannot be saturated the contribution of high intensity, and magnetic flux density is caused to reduce.Cause
This, is set as 0.06% or more and 0.20% or less for the range of Nb content.Preferably 0.08% or more and 0.18% or less.With
In the rolling direction for obtaining 550MPa or more yield strength preferred scope be 0.10% or more and 0.18% or less.
Surplus is Fe and inevitable impurity.
The above are in the present invention at being grouped as, can be according to following purposes into one on the basis of mentioned component composition
Step is containing V:0.01% more than or lower than 0.05%, Ti:0.01% more than or lower than one or more of 0.05%.
V and Ti is to facilitate the element of further high intensity in conjunction with C.The effect, preferably V and Ti in order to obtain
Contain 0.01% or more.When on the other hand, containing 0.05% or more V, the carbide containing V in welding heat affected zone
The influence of the caused softening of dissolution becomes significantly, and weldability reduces.Containing 0.05% or more Ti when, slab before hot rolling
The coarse carbide containing Ti is remained in heating process, and magnetic flux density is caused to reduce.Therefore, containing sometimes, it is set as V:
0.01% more than or lower than 0.05%, Ti:0.01% more than or lower than 0.05%.Preferably V:0.01% or more and 0.04% with
Under, 0.03% or less Ti:0.01% or more and.
Then, the restriction reason of the characteristic of magnetic pole of the invention hot rolled steel plate is illustrated.
The yield strength of rolling direction is 500MPa or more
For hydroelectric generation rim component etc., it is desirable that intensity.The yield strength of rolling direction is
When 500MPa or more, plate thickness can be reduced and be applied to efficient hydroelectric generation rim component.In this case, based on
The yield strength of the tension test in the parallel direction of rolling direction becomes important, therefore, carries out to the yield strength of rolling direction
Regulation.Steel plate particularly suitable for yield strength of the invention less than 700MPa.
Magnetic flux density B50For 1.4T or more, magnetic flux density B100For 1.5T or more
Magnetic flux density B50For 1.4T or more, magnetic flux density B100When for 1.5T or more, it to be used for hydroelectric generation rim component
In the case where, it can be realized hydroelectric high efficiency.
The minimum of the Vickers hardness of welding heat affected zone is (average value -30 of the Vickers hardness of base material) or more
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 base material), it is able to suppress the defect, bad of weld part.Welding condition at this time with
The condition recorded in embodiment is same.
Then, the manufacturing method of magnetic pole of the invention hot rolled steel plate is illustrated.
Magnetic pole of the invention can be manufactured by the following method with hot rolled steel plate: the steel former material (steel that mentioned component is formed
Base) heated at 1100 DEG C or more and 1350 DEG C or less, then, implement 1100 DEG C or more at a temperature of complete roughing and will
Final rolling temperature is set as 840 DEG C or more of hot rolling, with 30 DEG C/sec or more of average cooling rate within 3 seconds after finish rolling
It is cooling, then, batched at 550 DEG C or more and 700 DEG C or less.
In the present invention, the method for smelting of steel is not particularly limited, and can use the public affairs such as converter (converter), electric furnace
The method of smelting known.Furthermore it is possible to carry out double refining using vacuum degassing furnace (vacuum degassing furnace)
(secondary refining).Then, consider from the problem in productivity, quality, slab (steel is preferably made by continuous metal cast process
Former material), but ingot casting-split rolling method method (ingot casting and blooming), sheet blank continuous casting method etc. can also be passed through
Slab is made in well known casting method.
The heating temperature of steel former material: 1100 DEG C or more and 1350 DEG C or less
Before hot rolling, need that steel former material is heated and formed the austenite phase of substantial homogeneous.Heating temperature is low
When 1100 DEG C, the coarse carbide dissolution containing Nb and Ti, intensity and magnetic flux density cannot be reduced.On the other hand, add
When hot temperature is more than 1350 DEG C, oxide skin (scale) production quantity increases, and oxide skin, the surface of hot rolled steel plate are bitten in hot rolling
Character deterioration.Therefore, the heating temperature of steel former material is set as 1100 DEG C or more and 1350 DEG C or less.Preferably 1150 DEG C or more and
1300 DEG C or less.But when implementing hot rolling to steel former material, the steel former material after casting is below in 1100 DEG C or more and 1350 DEG C
In the case where temperature range or in the case that the carbide of steel former material dissolves, direct sending rolling can be carried out without to steel original
Material is heated.
1100 DEG C or more at a temperature of complete roughing and final rolling temperature be set as to 840 DEG C or more of hot rolling
C not in conjunction with Nb, V and Ti is precipitated in the form of Fe carbide.In order to make containing C almost all to contain
The form of the fine carbide of Nb, V and Ti is precipitated, and needs to complete the roughing before finish rolling at 1100 DEG C or more.This is because
In the case where being lower than 1100 DEG C of completion roughing, using the strain imported in roughing as driving force, due to keeping for a long time later
The carbide containing Nb, V and Ti is precipitated coarsely in austenite, this becomes the adverse effect for intensity and magnetic flux density
It obtains significantly.When final rolling temperature is lower 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 in the inside of the ferrite crystal grain of the stretching, extension, therefore, magnetic flux density are caused to reduce.Therefore, final rolling temperature
It is set as 840 DEG C or more.Preferably 860 DEG C or more.It should be noted that the temperature in finish rolling is lower than 1100 DEG C, but in finish rolling
Tandem rolling compared with roughing, the time for not being precipitated, growing, therefore, adverse effect when above-mentioned roughing is not significant.
It is cooled down after finish rolling within 3 seconds with 30 DEG C/sec or more of average cooling rate
Carbide containing Nb is miniaturize with from austenite to the low temperature of ferritic phase transition temperature.In order to obtain
Average grain diameter is 6nm carbide below, needs that 700 DEG C or less will be set as from austenite to ferritic phase transition temperature.For
This, needs to be cooled down after finish rolling within 3 seconds with 30 DEG C/sec or more of average cooling rate.It should be noted that flat
Equal cooling velocity is the average cooling rate from final rolling temperature to 700 DEG C.
Coiling temperature: 550 DEG C or more and 700 DEG C or less
When coiling temperature is more than 700 DEG C, carbide coarsening cannot obtain desired intensity and magnetic characteristic.On the other hand,
When lower than 550 DEG C, thus bainite phase reduces magnetic characteristic.Therefore, by the range of coiling temperature be set as 550 DEG C with
It is upper and 700 DEG C or less.Preferably 580 DEG C or more and 680 DEG C or less.
Magnetic pole hot rolled steel plate of the invention is manufactured by the above method.It should be noted that even if by magnetic of the invention
Pole is that logical plate is carried out in 720 DEG C of continuous hot-dipping production lines below in annealing temperature with hot rolled steel plate, to material also without shadow
It rings.Therefore, it can further implement plating to surface of steel plate and there is coating in surface of steel plate.In addition, plating, plating
The composition of bath will not affect material, therefore, as plating, can apply hot galvanizing processing, alloyed hot-dip
Zinc processing, electrogalvanizing processing in any one.In addition, the composition as 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.
It is suitable for requiring the component of high magnetic pole with hot rolled steel plate by magnetic pole of the invention obtained by the above method, especially
It is best suited for the use as hydroelectric generation rim component.For example, by hot rolled steel plate of the invention by shearing, being punched, swash
The methods of light cutting is cut into defined shape, is laminated, can be as the electromagnetism towards wheel rim, iron core (pole core etc.)
Component uses.In particular, hot rolled steel plate of the invention can be suitable for the hair for needing to take into account high intensity and good magnetic characteristic
Motor wheel rim.In the stacking of steel plate, insulating wrapped preferably is implemented between steel plate or sandwiched insulation raw material etc. make steel plate
It is electrically insulated between the steel plate of stacking and steel plate.
Embodiment 1
For with, at the steel former material for the wall thickness 250mm being grouped as, being made under the hot-rolled condition shown in table 2 shown in table 1
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 700 DEG C or less, the group of plating bath (molten bath) becomes Zn-0.13 mass %Al, the temperature of plating bath is 460
DEG C, alloying temperature be that 530 DEG C of continuous hot-dipping production line is manufactured, coating adhesion amount (coating weight) setting
For every 45~65g/m of single side2。
It is cut from by the hot rolled steel plate or alloyed hot-dip galvanized steel sheet of plate thickness 1.6mm~3.2mm obtained by the above method
Test film observes tissue by following methods, evaluates performance.
(i) structure observation
The area 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 that the mode of viewing surface is cut, and is corroded using 3% nital (nital)
(etching) metal structure for showing plate thickness central part is amplified to 400 times using sweep type optical microscopy, to 10
The visual field is shot.Ferritic phase is the tissue with the form for not observing corrosion trace, cementite in crystal grain.Pass through image
They are isolated bainite phase, martensitic phase, pearlite (pearlite) etc. other than ferritic phase by parsing, using relative to
The area ratio of field of view carries out asking calculation.When seeking calculation area, counted ferrite grain boundaries as a part of ferritic phase.
The average grain diameter of the carbide containing Nb about precipitation, using transmission electron microscope with 135000 times or more
It is observed, takes being averaged for the partial size of 100 points or more of carbide, find out partial size of the equivalent circle diameter as each carbide.
About Fe amount of precipitation, in 10%AA system electrolyte (- 1 quality % tetramethyl ammonium chloride of 10 volume % acetylacetone,2,4-pentanedione-first
Alcohol) in, will about 0.2g with 20mA/cm2Current density carry out constant-current electrolysis after, by filter from electrolyte trap be precipitated
Object finds out Fe amount contained in precipitate using ICP-MS method, the base steel after finding out and being electrolysed by constant-current electrolysis
Thus the ratio of quality obtains Fe amount of precipitation.
About Nb amount of precipitation (ratio is precipitated in Nb), constant current is carried out by the step same as the measuring method of Fe amount of precipitation
Electrolysis utilizes Nb amount contained in ICP-MS method measurement electrolyte.Nb amount is in solid solution condition contained in the electrolyte
Nb amount, Nb amount of precipitation are found out and subtracting the Nb amount in solid solution condition from Nb content.
(ii) tension test
From hot rolled steel plate or alloyed hot-dip galvanized steel sheet, JIS 5 drawings 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), find out 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 measures
The sample that 30mm × 280mm is cut from hot rolled steel plate or alloyed hot-dip galvanized steel sheet, is measured using DC Magnetic Properties
Device finds out magnetic flux density B by the measurement according to JIS C 255550With magnetic flux density B100。B50And B100Respectively indicate magnetization
Magnetic flux density under power 5000A/m and 10000A/m.
(iv) weldability is evaluated
As soldering test, evaluated using the CO2 welding of the wire of diameter 1.2mm.Welding
Condition be speed of welding be 80cm/ minutes, the butt welding of welding current 220A, weldingvoltage 25V, plate gap (gap) 1mm.
After welding, cut out welding seam part section, to the plate thickness central portion of its section with the interval 0.5mm relative to cross the direction of weld part into
Row test load is the Vickers hardness test of 0.49N.On the other hand, the test load pair that the hardness of base material is set as with 0.49N
Average value obtained from 5 points of position finding apart from weld part 30mm or more.Shown in table 3 base material hardness (base material hardness
Average value) and the minimum hardness (welding heat affected zone hardness minimum) in heat affected area difference.
The result obtained as described above is shown in Table 3.
Known to: the yield strength YS that example of the present invention has obtained rolling direction is 500MPa or more and welding heat affected
The minimum of the Vickers hardness in area is the weldability and magnetic flux density B of (average value -30 of the Vickers hardness of base material) or more50
For 1.4T or more, magnetic flux density B100For the hot rolled steel plate (alloyed hot-dip galvanized steel sheet) of the excellent in magnetic characteristics of 1.5T or more.It is another
Aspect deviates in the comparative example of the scope of the present invention, and 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 at be grouped as in terms of quality % containing C:0.02% or more and 0.12% or less,
Si:0.1% or more and 0.7% or less, Mn:0.8% or more and 1.6% or less, P:0.03% or less, S:0.005% or less,
Al:0.08% or less, N:0.006% or less, Nb:0.06% or more and 0.20% or less, surplus by Fe and inevitably it is miscellaneous
Texture at,
The ferritic phase of tissue is calculated as 98% or more with the area ratio,
The Fe of precipitation relative to Fe amount contained in steel be 0.22 mass % or less, be precipitated Nb relative to Nb amount contained in steel
Average grain diameter for 80 mass % or more, the carbide containing Nb being precipitated be 6nm hereinafter,
The yield strength of rolling direction is 500MPa or more, magnetic flux density B50For 1.4T or more, magnetic flux density B100For 1.5T with
On, the minimum of the Vickers hardness of welding heat affected zone is (average value -30 of the Vickers hardness of base material) or more.
2. magnetic pole hot rolled steel plate as described in claim 1, which is characterized in that further satisfaction following formula (1),
Wherein, %C, %Nb, %V, %Ti indicate 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 it is described at being grouped as on the basis of, with quality %
Meter is containing V:0.01% more than or lower than 0.05%, Ti:0.01% more than or lower than one or more of 0.05%.
4. a kind of manufacturing method of magnetic pole hot rolled steel plate, wherein will have ingredient according to any one of claims 1 to 3
The steel former material of composition heats under 1100 DEG C or more and 1350 DEG C of temperature below, then, implements the temperature at 1100 DEG C or more
The lower hot rolling completed roughing and final rolling temperature is set as to 840 DEG C or more, with 30 DEG C/sec or more within 3 seconds after finish rolling
Average cooling rate cooled down, then, batched under 550 DEG C or more and 700 DEG C of temperature below.
5. the manufacturing method of magnetic pole hot rolled steel plate as claimed in claim 4, which is characterized in that further real to surface of steel plate
Apply plating.
6. the manufacturing method of magnetic pole hot rolled steel plate as claimed in claim 5, which is characterized in that the plating is hot dip
Any one of zinc processing, alloyed zinc hot dip galvanized processing, electrogalvanizing processing.
7. such as the manufacturing method of magnetic pole hot rolled steel plate described in claim 5 or 6, which is characterized in that in the plating
The composition of the coating of middle formation contains one or more of Zn, Si, Al, Ni, Mg.
8. a kind of hydroelectric generation rim component, by magnetic pole according to any one of claims 1 to 3 hot rolled steel plate structure
At.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014246562 | 2014-12-05 | ||
| JP2014-246562 | 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 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107002196A CN107002196A (en) | 2017-08-01 |
| CN107002196B true CN107002196B (en) | 2019-01-01 |
Family
ID=56091287
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201580065641.8A Active CN107002196B (en) | 2014-12-05 | 2015-11-20 | Magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component |
Country Status (5)
| Country | Link |
|---|---|
| JP (1) | JP6020769B1 (en) |
| KR (1) | KR101966313B1 (en) |
| CN (1) | CN107002196B (en) |
| MX (1) | MX2017007019A (en) |
| WO (1) | WO2016088321A1 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| MX2022010760A (en) * | 2020-05-08 | 2022-09-23 | Nippon Steel Corp | Hot rolled steel sheet and method for producing same. |
| 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 |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
-
2015
- 2015-11-20 WO PCT/JP2015/005806 patent/WO2016088321A1/en active Application Filing
- 2015-11-20 CN CN201580065641.8A patent/CN107002196B/en active Active
- 2015-11-20 MX MX2017007019A patent/MX2017007019A/en unknown
- 2015-11-20 KR KR1020177013924A patent/KR101966313B1/en active IP Right Grant
- 2015-11-20 JP JP2016512156A patent/JP6020769B1/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20170072312A (en) | 2017-06-26 |
| KR101966313B1 (en) | 2019-04-05 |
| JP6020769B1 (en) | 2016-11-02 |
| JPWO2016088321A1 (en) | 2017-04-27 |
| CN107002196A (en) | 2017-08-01 |
| WO2016088321A1 (en) | 2016-06-09 |
| MX2017007019A (en) | 2017-08-14 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109642281B (en) | High-strength cold-rolled steel sheet and method for producing same | |
| JP6179676B2 (en) | High strength steel plate and manufacturing method thereof | |
| JP4874333B2 (en) | High-strength hot-rolled steel sheet with no occurrence of peeling and excellent surface properties and burring properties and method for producing the same | |
| CN106574340B (en) | The manufacture method of high-strength steel sheet and its manufacture method and high strength galvanized steel plate | |
| CN107148486B (en) | High-strength steel sheet, high-strength hot-dip zinc-coated steel sheet, high-strength hot aludip and high-intensitive plated steel sheet and their manufacturing method | |
| KR101555418B1 (en) | Hot-rolled steel sheet and manufacturing method thereof | |
| JP6501045B1 (en) | Hot pressed member, method for producing the same, cold rolled steel sheet for hot pressing, and method for producing the same | |
| CN105143485A (en) | High-strength hot-rolled steel sheet and method for manufacturing same | |
| CN110177896A (en) | Steel plate and its manufacturing method | |
| CN109154045A (en) | Coated steel sheet and its manufacturing method | |
| WO2013018741A1 (en) | High-strength steel sheet having excellent shape-retaining properties, high-strength zinc-plated steel sheet, and method for manufacturing same | |
| CN105518173A (en) | Hot stamp molded body and method for producing same | |
| CN106133180B (en) | Drop stamping steel | |
| CN106133153B (en) | Drop stamping steel | |
| CN108486501A (en) | A kind of 1000MPa grade cold rolling hot dip galvanizings dual phase steel and its manufacturing method with enhancing plasticity | |
| JP2011111670A (en) | HIGH STRENGTH STEEL SHEET EXCELLENT IN DUCTILITY AND BENDABILITY AND HAVING MAXIMUM TENSILE STRENGTH OF >=900 MPa, METHOD FOR PRODUCING HIGH STRENGTH COLD ROLLED STEEL SHEET, AND METHOD FOR PRODUCING HIGH STRENGTH GALVANIZED STEEL SHEET | |
| JP2012001775A (en) | High-strength hot-rolled steel sheet excelling in burring property, and method for manufacturing the same | |
| US20190271051A1 (en) | High-strength steel sheet and method for producing same | |
| CN105308203A (en) | Cold-rolled steel sheet, galvanized cold-rolled steel sheet, and method for producing same | |
| CN110249067A (en) | Hot-dip galvanized steel sheet and its manufacturing method | |
| CN107002195B (en) | Magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component | |
| CN107002196B (en) | Magnetic pole hot rolled steel plate and its manufacturing method and hydroelectric generation rim component | |
| CN110331335A (en) | The high tensile hot rolled steel sheet of tensile strength with 780MPa or more | |
| JP6086079B2 (en) | High strength high yield ratio cold rolled steel sheet and method for producing the same | |
| CN108884532A (en) | High-strength hot-dip galvanized steel sheet and its manufacturing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |