WO2022244701A1 - 鉄系合金箔及びその製造方法、並びにそれを用いた部品 - Google Patents
鉄系合金箔及びその製造方法、並びにそれを用いた部品 Download PDFInfo
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- WO2022244701A1 WO2022244701A1 PCT/JP2022/020256 JP2022020256W WO2022244701A1 WO 2022244701 A1 WO2022244701 A1 WO 2022244701A1 JP 2022020256 W JP2022020256 W JP 2022020256W WO 2022244701 A1 WO2022244701 A1 WO 2022244701A1
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- inclusions
- alloy foil
- iron
- rolling
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 89
- 239000000956 alloy Substances 0.000 title claims abstract description 89
- 239000011888 foil Substances 0.000 title claims abstract description 79
- 238000004519 manufacturing process Methods 0.000 title claims description 22
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 title abstract 3
- 229910052751 metal Inorganic materials 0.000 claims abstract description 70
- 239000002184 metal Substances 0.000 claims abstract description 70
- 229910052742 iron Inorganic materials 0.000 claims abstract description 55
- 239000002245 particle Substances 0.000 claims abstract description 31
- 239000000203 mixture Substances 0.000 claims abstract description 24
- 239000012535 impurity Substances 0.000 claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 115
- 238000005096 rolling process Methods 0.000 claims description 91
- 239000000463 material Substances 0.000 claims description 39
- 229910000831 Steel Inorganic materials 0.000 claims description 29
- 238000005097 cold rolling Methods 0.000 claims description 29
- 239000010959 steel Substances 0.000 claims description 29
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 19
- 238000005098 hot rolling Methods 0.000 claims description 19
- 239000000725 suspension Substances 0.000 claims description 7
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 3
- 238000007789 sealing Methods 0.000 claims description 3
- 238000005530 etching Methods 0.000 abstract description 25
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 14
- 229910052782 aluminium Inorganic materials 0.000 abstract description 12
- 229910052749 magnesium Inorganic materials 0.000 abstract description 11
- 229910052710 silicon Inorganic materials 0.000 abstract description 11
- 229910052791 calcium Inorganic materials 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 3
- 229910052593 corundum Inorganic materials 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 238000000034 method Methods 0.000 description 30
- 229910052596 spinel Inorganic materials 0.000 description 20
- 239000011029 spinel Substances 0.000 description 20
- 239000011651 chromium Substances 0.000 description 17
- 235000013339 cereals Nutrition 0.000 description 16
- 238000002844 melting Methods 0.000 description 16
- 230000008018 melting Effects 0.000 description 16
- 238000012360 testing method Methods 0.000 description 16
- 229910052717 sulfur Inorganic materials 0.000 description 15
- 229910004298 SiO 2 Inorganic materials 0.000 description 13
- 238000011156 evaluation Methods 0.000 description 13
- 230000007547 defect Effects 0.000 description 11
- 229910052748 manganese Inorganic materials 0.000 description 10
- 238000005259 measurement Methods 0.000 description 9
- 229910052760 oxygen Inorganic materials 0.000 description 8
- 238000007711 solidification Methods 0.000 description 8
- 230000008023 solidification Effects 0.000 description 8
- 239000007789 gas Substances 0.000 description 7
- 150000003568 thioethers Chemical class 0.000 description 7
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- 238000005242 forging Methods 0.000 description 6
- 238000009689 gas atomisation Methods 0.000 description 6
- 239000000843 powder Substances 0.000 description 6
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 5
- ODINCKMPIJJUCX-UHFFFAOYSA-N calcium oxide Inorganic materials [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 5
- 230000006698 induction Effects 0.000 description 5
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 238000011282 treatment Methods 0.000 description 5
- 230000002776 aggregation Effects 0.000 description 4
- SNAAJJQQZSMGQD-UHFFFAOYSA-N aluminum magnesium Chemical compound [Mg].[Al] SNAAJJQQZSMGQD-UHFFFAOYSA-N 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 4
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- 238000001513 hot isostatic pressing Methods 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 230000002411 adverse Effects 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
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- 230000000694 effects Effects 0.000 description 3
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 3
- VASIZKWUTCETSD-UHFFFAOYSA-N manganese(II) oxide Inorganic materials [Mn]=O VASIZKWUTCETSD-UHFFFAOYSA-N 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- 238000007740 vapor deposition Methods 0.000 description 3
- 229910000640 Fe alloy Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910001374 Invar Inorganic materials 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
- 238000004220 aggregation Methods 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000012937 correction Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000011819 refractory material Substances 0.000 description 2
- 238000012552 review Methods 0.000 description 2
- 238000001878 scanning electron micrograph Methods 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000002893 slag Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- CFJRGWXELQQLSA-UHFFFAOYSA-N azanylidyneniobium Chemical compound [Nb]#N CFJRGWXELQQLSA-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- DBULDCSVZCUQIR-UHFFFAOYSA-N chromium(3+);trisulfide Chemical compound [S-2].[S-2].[S-2].[Cr+3].[Cr+3] DBULDCSVZCUQIR-UHFFFAOYSA-N 0.000 description 1
- 229910052681 coesite Inorganic materials 0.000 description 1
- 229910052906 cristobalite Inorganic materials 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 230000000873 masking effect Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000000149 penetrating effect Effects 0.000 description 1
- 238000001259 photo etching Methods 0.000 description 1
- 229920002120 photoresistant polymer Polymers 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000000377 silicon dioxide Substances 0.000 description 1
- 235000012239 silicon dioxide Nutrition 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 241000894007 species Species 0.000 description 1
- 229910052682 stishovite Inorganic materials 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 229910052905 tridymite Inorganic materials 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
Images
Classifications
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- B22F3/17—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by forging
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- 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
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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
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- 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
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
- B22F5/006—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of flat products, e.g. sheets
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/30—Stress-relieving
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- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
Definitions
- the present invention relates to an iron-based alloy foil, a method for manufacturing the same, and parts using the iron-based alloy foil.
- it can be applied to electronic device parts such as metal masks and hard disk drive suspensions, and parts for manufacturing electronic devices.
- OLEDs organic light-emitting diodes
- HDD hard disk drives
- the pitch between the mask holes is at least the same as the pixel density of the OLED, and the mask holes The pore size is also reduced accordingly.
- the mask hole of a metal mask has a truncated cone shape (the cross section is tapered).
- the cross section is tapered.
- etching defects may occur. For example, if an inclusion having a size equal to or larger than half the plate thickness of the metal plate is present in the portion where the mask hole is formed, the metal portion around the inclusion is dissolved when half-etching is performed from one side. Then, the part where the dry film is arranged on the opposite side surface is also dissolved, and the dry film on the opposite side is peeled off. Then, when the metal plate is half-etched from the opposite side, the portion of the metal plate where the dry film is peeled off is also etched, resulting in a state in which irregular-shaped holes are formed centering on the inclusions.
- etching defects caused by such inclusions become more pronounced as the pixel density of the manufactured OLED increases.
- the metal mask is formed by etching a metal plate having a thickness similar to the pitch interval corresponding to the pixel density of the manufactured OLED. Therefore, in the case of an OLED with a pixel density of 800 to 1000 PPI, it will be necessary to reduce the thickness of the metal mask from the current 20.00 to 30.00 ⁇ m to 12.00 to 15.00 ⁇ m. For this reason, it is necessary to limit the size of inclusions to less than 10.00 ⁇ m.
- Inclusions are mainly hard inclusions such as alumina (Al 2 O 3 ) and magnesium-aluminum spinel (MgO.Al 2 O 3 ), and soft inclusions such as silica (SiO 2 ) and CaO. .
- Hard inclusions have high interfacial energy and tend to agglomerate, and tend to increase in size after agglomeration.
- hard inclusions are difficult to be refined by hot rolling or cold rolling, and as a result, they remain as inclusion particles having a large size. Therefore, it is important to reduce the size of the inclusions contained in the metal plate and reduce the number of particles in order to improve etching defects associated with high-precision processing.
- Patent Documents 1 and 2 propose using an Invar alloy.
- Patent Document 1 discloses a method for manufacturing a metal mask for OLED with a plate thickness of about 100.00 ⁇ m, in which an Fe—Ni alloy is subjected to vacuum melting, forging, hot rolling, cold rolling, and intermediate annealing in this order.
- Patent Document 2 discloses that in order to reduce the oxygen concentration of the molten metal, the purity of the molten metal is increased by vacuum induction melting or the like, and then the ingot is cast, thereby preventing defective etching of the metal mask material. .
- molten metal molten alloy
- tundish or melting furnace molten metal
- Billets produced by continuous casting and vacuum melting take time to completely solidify. Therefore, a steel slab manufactured by continuous casting and vacuum melting solidifies from the outside while the center remains in a melted state, so inclusions tend to segregate and solidify inside the steel slab.
- the alumina and spinel remaining in the molten metal have high interfacial energies, so they tend to cluster and form coarse inclusions during cooling of the molten metal.
- Patent Documents 3 and 4 estimate the size of the maximum nonmetallic inclusions in the Fe—Ni alloy slab, and the etching process that can clarify the quality history of the finally obtained rolled sheet and coil. Disclosed is a method for manufacturing an Fe—Ni alloy plate for However, in Patent Documents 3 and 4, Fe—Ni alloy ingots are produced by casting by a conventional ingot casting method or by continuous casting. Therefore, the steel slab manufactured by the manufacturing methods disclosed in Patent Documents 3 and 4 takes time to completely solidify, so inclusions tend to segregate and solidify inside the steel slab.
- Patent Document 5 a steel ingot of an Fe-31%Ni-5%Co super invar alloy is produced by a vacuum induction melting furnace, then heated to 1100° C. for solution treatment, forging and hot rolling. After performing a niobium nitride precipitation treatment at 800 to 900° C. as a sheet material, cold rolling and annealing are repeated to produce a cold rolled material with a thickness of 0.1 mm.
- a vacuum induction melting furnace After performing a niobium nitride precipitation treatment at 800 to 900° C. as a sheet material, cold rolling and annealing are repeated to produce a cold rolled material with a thickness of 0.1 mm.
- Patent Document 6 discloses a stainless steel plate suitable for precision equipment members such as HDD (hard disk drive) members and thin-film silicon solar cell substrates.
- the presence of minute pits distributed on the surface of a stainless steel plate greatly affects the washability of the stainless steel plate. It is disclosed that these minute pits are caused by inclusions and traces of carbonized particles falling off during the rolling process.
- MgO—Al 2 O 3 -based inclusions have low deformability in the cold rolling process, voids and gaps are likely to occur at the metal/inclusion interface, and they become starting points for micropits and cracks. described as easy.
- non-metallic inclusions mainly composed of Mn(O,S)--SiO 2 and adjusting MgO and Al 2 O 3 to a predetermined concentration or less, the non-metallic inclusions are rendered harmless. It is disclosed that the
- Patent Document 7 in an Fe—Ni alloy plate for a vapor deposition mask, the number of particles of 1 ⁇ m or more per 1 mm 3 is 3000 or less, the number of particles of 3 ⁇ m or more is 50 or less, and the total number of particles of 1 ⁇ m or more. It discloses a metal plate having a number ratio of 1 to 3 ⁇ m particles to 70% or more.
- the metal plate manufacturing method disclosed in Patent Document 7 is based on the premise that inclusions float during solidification during ingot manufacturing, and segregation that occurs during the normal solidification process (especially segregation to the center of the ingot) ) is not taken into consideration, so it cannot be applied to actual metal plate manufacturing. Therefore, Patent Document 7 essentially discloses only the selection criteria that a person skilled in the art would naturally perform, that is, a metal plate with few coarse inclusions is selected and used as a metal plate for a vapor deposition mask.
- etching defects caused by inclusions become more pronounced as electronic components become more precise or downsized.
- the higher the pixel density of manufactured OLEDs the smaller the suspension for HDDs, the more pronounced.
- the present inventors have conducted intensive research into the relationship between the size of inclusions and poor etching of metal mask materials. As a result, it was found that when the thickness of the metal mask material is as thin as about 10.00 ⁇ m, if inclusions larger than 5.00 ⁇ m are reduced, defective etching of the metal mask material can be reduced.
- pinholes are reduced by reducing inclusions with a particle size of greater than 5.00 ⁇ m contained in the metal mask material.
- an object of the present invention is to reduce the number of coarse inclusions having a grain size of more than 5.00 ⁇ m in an ultrathin iron alloy foil having a thickness of 10.00 ⁇ m or more, and an iron-based alloy foil with reduced coarse inclusions. , its manufacturing method, and parts using it. Inclusions having a grain size of more than 5.00 ⁇ m are hereinafter referred to as coarse inclusions unless otherwise specified.
- the inventors focused on Al 2 O 3 , MgO, SiO 2 , CaO, Mn(O, S), and CrS as basic components of inclusions.
- inclusions made of at least one of SiO 2 , CaO, Mn(O, S), and CrS are difficult to cluster and have a low melting point and are soft. It was found that crushing reduces coarse inclusions. (SiO 2 , CaO, Mn(O, S), and CrS are sometimes called soft inclusions.)
- inclusions such as alumina (Al 2 O 3 ) and magnesium-aluminum spinel (MgO.Al 2 O 3 , hereinafter sometimes referred to as spinel) have high interfacial energy and segregate and aggregate during solidification. , the size after agglomeration tends to increase. Furthermore, since inclusions of alumina and spinel are hard, the inclusions are difficult to be crushed during hot rolling or cold rolling, and as a result, they remain as inclusion particles having a large size. (Alumina and magnesium-aluminum spinel are sometimes called hard inclusions.)
- the ratio of alumina and spinel contained in the inclusions is reduced, the manufacturing conditions of the iron alloy foil, especially the rolling conditions, are reviewed, the number of coarse alumina and spinel inclusions is reduced, and the soft inclusions are finely divided. It was found that an iron-based alloy foil with reduced coarse inclusions can be obtained by dispersing them.
- the present invention was made based on the above findings, and the gist thereof is as follows.
- the iron-based alloy foil according to any one of (1) to (4), wherein the surface of the iron-based alloy foil has a pinhole density of 5/1000 m 2 or less with a diameter of 20 ⁇ m or more.
- the iron-based alloy foil in % by mass, C: 0.150% or less, Si: 0.1 to 2.00%, Mn: 0.10-1.20%, S: 0.007% or less, Ni: 2.00 to 15.00%, Cr: 15.00 to 19.00%, N: 0.20% or less, Al: 0.010% or less, An austenitic stainless steel with the balance being Fe and impurities, having a density of 5 pinholes/1000 m 2 or less with a diameter of 20 ⁇ m or more on the surface, and a 0.2% proof stress of 700 MPa or more.
- the iron-based alloy foil according to (1) (7)
- a metal mask material comprising the iron-based alloy foil according to any one of (1) to (7).
- (10) A part having the iron-based alloy foil according to any one of (1) to (7).
- (11) A hard disk drive suspension comprising the iron-based alloy foil according to any one of (1) to (7).
- an iron-based alloy foil in which coarse inclusions are reduced and defects are less likely to occur during rolling and etching. Furthermore, when applied to metal masks and suspensions for hard disks, etching defects can be remarkably reduced, enabling high-precision processing with high yield. Furthermore, such high-precision processing can result in more downsized electronic components.
- FIG. 1 is an example for verifying the validity of the evaluation area of inclusions on the surface of an alloy foil, and is a diagram showing variations in the number density of inclusions with respect to the measured area.
- the iron-based alloy foil of the present invention is, in mass %, C: 0.150% or less, Si: 2.00% or less, Mn: 10.00% or less, Ni: 2.00 to 50.00%, Cr : 19.00% or less, N: 0.20% or less, Al: 0.030% or less, Co: 5.00% or less, Mg: 0.0005% or less, Ca: 0.0005% or less, Ti: 0 0.01% or less, P: 0.035% or less, S: 0.0300% or less, and the balance being Fe and impurities.
- Ni has effects of improving corrosion resistance and workability, and is a main element for adjusting the thermal expansion coefficient of the alloy.
- the Ni content should be 2.00% or more.
- the Ni content is 5.00% or more, 10.00% or more, 15.00% or more, 20.00% or more, 25.00% or more.
- the Ni content is preferably 30.00% or more, 31.00% or more, 32.00% or more, 34.00% or more, or 35.00% or more.
- Ni is an expensive element, and if the Ni content is too high, a bainite structure tends to form in the steel after hot rolling or hot forging. Therefore, the Ni content is preferably 50.00% or less, 45.00% or less, 40.00% or less, 38.00% or less, or 37.00% or less.
- Cr is an alloy component necessary for improving corrosion resistance. However, if Cr is contained excessively, the steel material becomes hard and workability deteriorates, so the Cr content should be 19.00% or less.
- the lower limit of the Cr content is not particularly limited and may be 0%. On the other hand, when the Cr content is 15.00% or more, the effect of adding Cr becomes remarkable, so the Cr content is preferably 15.00% or more.
- Co is a component that can further reduce the coefficient of thermal expansion of the alloy when the amount added is increased in relation to the amount of Ni.
- Co may not be contained, but if Co is contained, it is preferably 0.01% or more, 0.02% or more, or 0.05% or more.
- the upper limit of the Co content should be 5.00%, preferably 4.00% or less, or 3.00% or less.
- C carbon
- C carbon
- it may be contained because it increases the strength of metal foils such as metal mask materials. If C is contained, it should be 0.001% or more, 0.003% or more, 0.005% or more, 0.010% or more, or 0.020% or more. However, if C is contained excessively, the coefficient of thermal expansion increases, and Cr-based inclusions (Cr carbides) precipitated at grain boundaries increase, causing pinholes. Therefore, the C content should be 0.150% or less, preferably 0.100% or less, or 0.050% or less.
- Ca forms a solid solution in sulfides, finely disperses the sulfides, and spheroidizes the sulfides.
- Ca may not be contained, but if Ca is contained, the Ca content should be 0.0001% or more, or 0.0002% or more. On the other hand, if a large amount of Ca is contained, Ca that does not form a solid solution in the sulfide may form coarse oxides, resulting in poor etching. Therefore, the Ca content should be 0.0005% or less, preferably 0.0004% or less.
- Mn is actively used as a deoxidizer instead of Mg and Al to avoid spinel formation.
- the Mn content is preferably 10.00% or less, preferably 5.00% or less, 2.00% or less, 1.50% or less, 1.20% or less, 1.00% or less, and 0.80%. % or less, 0.60% or less, 0.50% or less, 0.40% or less, or 0.30% or less.
- Mn may not be included. However, if the Mn content is too small, it becomes difficult to adjust the composition of inclusions to a Mn(O,S)—SiO 2 system composition.
- the Mn content is preferably 0.01% or more, 0.03% or more, 0.05% or more, or 0.10% or more.
- Mn(O, S) refers to MnO simple substance, MnS simple substance, and inclusions in which MnO and MnS are combined. It means an inclusion.
- Si is positively used as a deoxidizer instead of Mg and Al in order to avoid formation of spinel.
- Si increases the thermal expansion coefficient of the alloy.
- the metal mask material is sometimes used in a temperature environment of about 200° C. so that the organic EL light-emitting material emitted from the vapor deposition source can pass through the mask holes.
- the deoxidation product MnO—SiO 2 is a vitrified soft inclusion, which is elongated and split during hot rolling to be refined. Therefore, the hydrogen embrittlement resistance is enhanced.
- the Si content exceeds 2.00%, the strength becomes too high and the steel is hardened. sexuality is greatly reduced.
- the Si content should be 2.00% or less, preferably 1.00% or less, 0.50% or less, or 0.30% or less. Si may not be included. However, if it is too small, deoxidation will be insufficient, and the concentration of Cr 2 O 3 in inclusions will increase, making it easier to generate inclusions that induce work cracks. Therefore, the Si content is preferably 0.01% or more, 0.03% or more, 0.05% or more, or 0.10% or more.
- Mg is used for deoxidizing steel. However, if the Mg content exceeds 0.0005%, coarse inclusions may form. In addition, since it is preferable that the content of Mg is low in order to avoid the formation of spinel, it may not be included. Therefore, the Mg content should be 0.0005% or less, preferably 0.0003% or less, 0.0002% or less, or 0.0001% or less.
- Al is also used for deoxidizing steel. However, if the Al content exceeds 0.030%, coarse inclusions may form. Also, the Al content is preferably as low as possible in order to avoid spinel formation. Therefore, the Al content should be 0.030% or less, preferably 0.020% or less, 0.010% or less, or 0.005% or less.
- P and S are elements that combine with alloying elements such as Mn in iron-based alloys to form inclusions, so the smaller the content, the better, so they do not have to be included. Therefore, the P content should be 0.035% or less, preferably 0.010% or less, 0.007% or less, or 0.005% or less, and the S content should be 0.0300% or less, preferably 0.005% or less. 0100% or less, 0.0070% or less, or 0.0050% or less.
- Ti increases the coefficient of thermal expansion of the alloy, it is preferable that it is low. Therefore, Ti does not have to be contained, but its content should be 0.01% or less.
- N is also a solid-solution strengthening element.
- the 0.2% yield strength increases, but the steel material hardens and the manufacturability remarkably deteriorates. Therefore, N may not be included, and the upper limit of the N content should be 0.20%, preferably 0.10% or less.
- the balance of the above steel components is Fe and unavoidable impurities.
- the unavoidable impurities are components that are mixed due to various factors in the manufacturing process, including raw materials such as ores and scraps, when steel is manufactured industrially, and have an adverse effect on the present invention. It means what is permissible within the scope of
- inclusions There should be few inclusions, ideally none at all. However, since it is mixed in during the manufacturing process or generated from steel components, it is not easy to eliminate it completely. As described above, when used as a material for a metal mask or the like, inclusions having a size of about half of the plate thickness are harmful because they cause poor etching. Furthermore, it has been found that coarse inclusions on the surface fall off during rolling and tend to cause pinholes and surface pits. Therefore, in the case of inclusions with a large grain size, for example, an ultra-thin alloy foil with a plate thickness of 10 ⁇ m, it is important to reduce inclusions with a circle-equivalent grain size of 5 ⁇ m or more as much as possible.
- the inventors focused on Al 2 O 3 , MgO, SiO 2 , CaO, Mn(O, S), and CrS as basic components of inclusions.
- soft inclusions such as SiO 2 , CaO, Mn(O, S), and CrS are hard to cluster and have a low melting point and are soft, so they are stretched or crushed by rolling, and coarsening is suppressed. rice field.
- hard inclusions such as alumina and magnesium-aluminum spinel have high interfacial energy and tend to segregate and agglomerate during the solidification process.
- inclusions of alumina and spinel are hard, so that they are difficult to be stretched or crushed during rolling, and as a result, they remain as inclusion particles with a large size.
- the steel components in order to ensure the mechanical strength of the alloy foil without forming inclusions in both soft and hard alloy foils, it is preferable to use the steel components as described above. In order not to mix inclusions, it is important to review the process. For example, it is recommended to review the refractories used for molten metal treatment and use refractories containing less Al and Mg. Furthermore, one of the causes of the aggregation of inclusions is, for example, segregation and aggregation during solidification from molten metal. It is not easy to avoid segregation during solidification. Furthermore, the ingot may be produced by a process that does not use a solidification process from molten metal, such as HIP (Hot Isostatic Pressing). The manufacturing process will be explained later.
- HIP Hot Isostatic Pressing
- Inclusions contained in the iron-based alloy foil of one aspect of the present invention are inclusions having a particle size (equivalent circle diameter) of 2.00 ⁇ m or more for measurement reasons (hereinafter simply referred to as “inclusions” unless otherwise specified). There are cases.) is targeted. Coarse inclusions with a grain size of more than 5.00 ⁇ m are harmful and should be reduced as much as possible. On the other hand, inclusions with a particle size of 2.00 to 5.00 ⁇ m are preferably reduced, but are not directly harmful.
- the number of inclusions with a grain size of 2.00 to 5.00 ⁇ m is preferably 80.00% or more of the total number of inclusions with a grain size of 2.00 ⁇ m or more. It is preferably 85.00% or more, 90.00% or more, 95.00% or more, 97.00% or more, 98.00% or more, 99.00% or more, or 100%.
- Al 2 O 3 should be 30% by mass or less and MgO should be 15% by mass or less with respect to the total mass of inclusions having a grain size of 2.00 ⁇ m or more. Since these hard inclusions are preferably as small as possible, the ratio of Al 2 O 3 is preferably 25% or less, 20% or less, 15% or less, 10% or less, 5% or less, 3% or less, or 1%. It should be below. Similarly, the proportion of MgO is preferably 10% or less, 8% or less, 6% or less, 5% or less, 4% or less, 3% or less, 2% or less, or 1% or less.
- the inclusion size is measured as follows. Inclusions on the surface of the metal foil are observed using a scanning electron microscope (SEM). As the SEM, for example, JSM-IT500HR manufactured by JEOL Ltd. may be used. An example of SEM settings is shown. ⁇ Detector: Backscattered electron detector BED-C ⁇ Observation magnification: 80 times ⁇ Acceleration voltage: 20.0 kV ⁇ Working distance (WD): 10.0 mm ⁇ Irradiation current: 80% Inclusions were detected from the image acquired by the SEM using inclusion automatic analysis software, and composition analysis of the inclusions was performed using an energy dispersive X-ray spectrometer (hereinafter referred to as an EDS device).
- EDS device energy dispersive X-ray spectrometer
- the particle analysis mode of AZtec manufactured by Oxford may be used.
- the EDS apparatus may be ULTIM MAX 65 manufactured by Oxford, for example.
- the step of identifying inclusions by the inclusion automatic analysis software first, an SEM image used in the inclusion automatic analysis software is obtained. Next, from the image acquired by the SEM, the inclusion automatic analysis software shows that the equivalent circle diameter (equivalent circle equivalent diameter) is 2.00 ⁇ m or more, and the elements of Al, Mg, Si, Ca, Mn, and S are determined by EDS. If one or more of these are detected, they are identified as inclusions. Images for which EDS analysis has been completed are combined on software and output as one image.
- the circle-equivalent diameter and elemental composition of inclusions identified by the inclusion automatic analysis software are also obtained. Measurement is performed up to the set area by repeating the procedure for identifying inclusions described above.
- the measurement area of the image may be 10 cm 2 as one field of view, which is the unit of measurement, and 10 fields of view may be measured, and a total of 100 cm 2 may be used as the evaluation area.
- the diameter of a circle having the same area as the measured inclusion area is defined as the equivalent circle diameter (equivalent circle diameter), which is defined as the "grain size".
- the inclusion composition is calculated as follows for each inclusion identified by the inclusion automatic analysis software. First, the mass percentages of the elements Al, Mg, Si, Ca, Mn, Cr, and S obtained by EDS analysis are divided by their atomic weights to obtain apparent material amounts of the elements. Next, the above seven elements are converted into oxides or sulfides, which are basic components of inclusions. In inclusions, Al, Mg, Si and Ca are mainly present as oxides. Mn and Cr mainly exist as sulfides, and Mn may also exist as an oxide MnO. S may exist as a chromium sulfide CrS in addition to the aforementioned sulfide MnS.
- the apparent amount of S is greater than the apparent amount of Mn, the same amount of MnS as the apparent amount of Mn is present, and the apparent amount of Mn is subtracted from the apparent amount of S.
- the apparent amount of S is less than the apparent amount of Mn, the same amount of MnS as the apparent amount of S is present, and the apparent amount of S is subtracted from the apparent amount of Mn.
- a material amount of MnO is present.
- the apparent amount of Mn and the apparent amount of S are exactly the same, the amount of MnS is present in the same amount as the amount of Mn and S.
- the equivalent mass of oxides, etc. is derived by multiplying the respective molecular weights.
- Al 2 O 3 , MgO, SiO 2 , CaO, MnO, MnS, CrS (hereinafter, “oxides, etc.” In some cases, it is said.) Calculate the mass% equivalent of oxides, etc.
- the area of inclusions obtained by the automatic analysis software for inclusions is multiplied by the mass % equivalent to seven oxides, etc., and the inclusion area ⁇ m of Al 2 O 3 , MgO, SiO 2 , CaO, MnO, MnS, and CrS is obtained. Ask for 2 .
- the inclusion area is obtained for all the inclusions identified by the inclusion automatic analysis software, and the inclusion area is totaled for each of the above seven oxides or sulfides to obtain the total area of Al 2 O 3 , MgO to obtain the total area of , the total area of SiO2 , the total area of CaO, the total area of MnO, the total area of MnS, and the total area of CrS.
- the total sum of these seven areas is defined as the total area of all inclusions.
- the composition ratio (% by mass) of inclusions is calculated by dividing the total area of each oxide or the like by the total area of all inclusions.
- the area ratio of inclusions is obtained by dividing the total area of each oxide or the like or the total area of all inclusions by the evaluation area to obtain the area ratio of each oxide or the like or the area ratio of all inclusions.
- the total inclusion number density is derived by dividing the total number of inclusions observed in the measurement area kcm2 by the measurement area, where k is 1, 2 , 4, 5, 8, 10, 20, 25, 40, 50, 100 and 200.
- the number ratio of spinel-based inclusions is extremely reduced, coarse inclusions are unlikely to exist.
- Mn and Si are mainly used as deoxidizing agents, the number ratio of MnO—SiO 2 type inclusions increases. This is because MnO—SiO 2 based inclusions are difficult to form clusters, and since they have a low melting point and are soft, they are easily stretched or crushed in the hot rolling process or cold rolling process, and are unlikely to exist as coarse inclusions. is.
- the number density of inclusions having a particle size of more than 5.00 ⁇ m can be reduced to 15/cm 2 or less. Therefore, inclusions of a size that cause etching defects are reduced.
- the number of coarse inclusions having a particle size of more than 5.00 ⁇ m is preferably as small as possible, preferably 12/cm 2 or less, 10/cm 2 or less, 8/cm 2 or less, 6/cm 2 or less, 5/cm 2 or less. cm 2 or less.
- the thickness of the iron-based alloy foil is not particularly limited, the thickness is preferably 30.00 ⁇ m or less because the size of the ingot (ingot) is required to some extent in normal manufacturing processes.
- the thickness is preferably 27.50 ⁇ m or less, 25.00 ⁇ m or less, or 22.50 ⁇ m or less.
- the plate thickness is less than 10.00 ⁇ m, handling becomes more difficult during etching or rolling, and defects such as wrinkles may occur.
- the 0.2% yield strength can be made 700 MPa or more. If the 0.2% proof stress of 700 MPa or more is obtained, it can be applied to a metal mask or the like without bending under normal use conditions.
- the iron-based alloy foil according to the present invention can be produced, for example, as follows. The methods presented below are exemplary and not intended to be limiting.
- a raw material adjusted to a predetermined composition is vacuum melted in a vacuum atmosphere of 10 ⁇ 1 (Torr) or less to obtain a molten metal having a desired alloy composition.
- Mn and Si are added so that the contents of Mn and Si in the molten metal after the slag removal are respectively predetermined contents.
- atomization is performed by gas atomization using an inert gas such as Ar or N2 gas.
- the temperature of the molten metal during gas atomization is preferably in the range of +50° C. to 200° C. in order to lower the viscosity of the molten metal.
- the ratio of gas flow rate (m 3 /min)/melt flow rate (kg/min) during gas atomization is preferably 0.3 (m 3 /kg) or more.
- the ratio of gas flow rate (m 3 /min)/molten metal flow rate (kg/min) is less than 0.3 (m 3 /kg), the cooling rate of the droplet becomes slow, so that the liquid when colliding with the ingot surface The liquid fraction of the droplets is too high and the inclusions become coarse. Therefore, the ratio of gas flow rate to molten metal flow rate is 0.3 (m 3 /kg) or more, preferably 0.5 or more, 0.7 or more, 0.9 or more, 1.0 or more, 1.5 or more, or 2 .0 or more is preferable.
- the upper limit of the ratio of gas flow rate (m 3 /min)/melt flow rate (kg/min) is not particularly limited, but the cooling capacity is saturated at 5.0 (m 3 /kg) or more, so the upper limit is 5.0. (m 3 /kg).
- the alloy powder obtained by the atomizing process is sintered by a hot press method or HIP method to produce an ingot.
- the sintering method is not particularly limited. Conditions may be appropriately set in accordance with a conventional hot press method or the like.
- the alloy powder preferably has a particle size of 300 ⁇ m or less, preferably 250 ⁇ m or less, 200 ⁇ m or less, 150 ⁇ m or less, or 100 ⁇ m or less.
- the content of Al and Mg can be suppressed by the atomizing (powdering) method described above. Furthermore, unlike the solidification method (casting method), the sintering method in which the refractory is processed in a solid phase does not contain Al or Mg from the refractory, so the formation of coarse (for example, 5 ⁇ m or more) inclusions is suppressed. As a result, Al 2 O 3 and spinel-based inclusions themselves are finally reduced, and in particular, the generation of coarse inclusions of 5 ⁇ m or more can be remarkably suppressed.
- the produced alloy ingot is hot forged, cut or ground to produce steel slabs.
- the steel slab is rolled to a thickness of 3.0 mm to 200 mm.
- the rolling may be hot rolling or cold rolling.
- the rolled sheet having a thickness of 3.0 mm to 200 mm is formed into an iron-based alloy foil by repeating the rolling process.
- the ingot may be annealed before and after hot rolling, hot forging, or cold rolling.
- the temperature in the annealing step, hot forging step and hot rolling step is a temperature below the melting point of the iron-based alloy in order to prevent inclusions from agglomerating, preferably the melting point temperature of the iron-based alloy -500 ° C. As described above, it is preferable that the melting point temperature of the iron-based alloy is in the range of ⁇ 200° C. or lower.
- Cold rolling should be performed after hot rolling or hot forging. Intermediate annealing may be performed during cold rolling. Rolling extends and crushes inclusions, especially soft inclusions, so that the inclusions can be made finer. Refinement of inclusions is more effective in cold rolling than in hot rolling, and when the plate thickness is thin. Therefore, it is preferable to set the total reduction ratio of cold rolling to 97.0% or more based on the plate thickness after hot rolling (plate thickness immediately before cold rolling). It is preferably 98.0% or more, 99.0% or more, or 99.5% or more.
- the rolling reduction in each rolling pass is 20% or more, except for the final rolling to make the target plate thickness and shape correction rolling.
- the soft inclusions can be expanded and crushed to be finer and dispersed.
- finish rolling after the plate thickness has been reduced to a certain extent and the inclusions have been refined to some extent, surface recesses and pinholes penetrating the alloy foil may be generated due to the falling off of the inclusions. I found out. Therefore, in finish rolling (multi-stage cold rolling) from 2 to 3 times the final thickness or from about 40 ⁇ m to the final thickness (for example, 10 ⁇ m or 20 ⁇ m), mild rolling with a low rolling reduction is recommended. For example, it is preferable to set the rolling reduction in each pass of the finish rolling to 1 to 18% and the cumulative rolling reduction to 50% or more. If the cumulative reduction in finish rolling is less than 50%, the strength of the alloy foil may not develop.
- the upper limit of the cumulative rolling reduction in finish rolling is not particularly limited, it is preferably 98% or less due to the capacity of a normal foil rolling mill. That is, the total rolling reduction in cold rolling is 97.0% or more, the cold rolling before finish rolling is 20% or more to refine soft inclusions, and the finish rolling is mild rolling to remove inclusions. should be suppressed.
- rolling (cold rolling) from a thickness of about 10 times the final thickness to the final thickness is called foil rolling, and is sometimes distinguished from cold rolling after hot rolling. In this case, it is more preferable to decrease the rolling reduction in order of cold rolling after hot rolling, subsequent foil rolling up to finish rolling, and final finish rolling.
- the rolling reduction of each pass should be 40% or more for cold rolling after hot rolling, 20% or more for foil rolling before finish rolling, and less than 20% for finish rolling in foil rolling.
- the draft is expressed by the following formula, where t1 is the plate thickness before rolling and t2 is the plate thickness after rolling.
- Reduction rate (t1-t2)/t1
- the cumulative rolling reduction may be calculated by setting the plate thickness before finish rolling to t1 and the plate thickness after finish rolling to t2.
- the draft of each pass can be calculated by setting the plate thickness before each rolling pass to t1 and the plate thickness after the rolling pass to t2.
- the unit rolling load (kN/mm) of each pass in the finish rolling should be controlled within an appropriate range.
- the unit rolling load is obtained by dividing the load applied from the rolling rolls to the work material by the width of the work material.
- a preferable unit rolling load is 0.4 to 1.3 kN/mm.
- the unit rolling load is less than 0.4 kN/mm, there is little heat generated during rolling and the flexibility of the alloy foil, which is the work material, is reduced. More things fall off.
- the unit rolling load exceeds 1.3 kN/mm, the amount of heat generated during processing increases, but the amount of plastic deformation of the alloy foil itself increases, so cracks occur at the interface with inclusions, and many inclusions fall off. Become. Therefore, the unit rolling load may be controlled instead of the rolling reduction. Of course, the rolling reduction and the unit rolling load may be combined for control.
- annealing may be performed for strain relief after finish rolling (final rolling).
- non-magnetic properties are required. That is, in mass%, C: 0.150% or less, Si: 0.1 to 2.00%, Mn: 0.10 to 1.20%, S: 0.007% or less, Ni: 2.00 Austenitic stainless steel containing ⁇ 15.00%, Cr: 15.00 to 19.00%, N: 0.20% or less, Al: 0.010% or less, and the balance being Fe and impurities. Also in this case, as in the above description, alumina and spinel-based inclusions can be reduced, and an alloy foil with good etching properties and excellent high-precision workability can be obtained.
- Example 1 For test materials 1, 2, and 4, a molten metal having an iron-based alloy composition adjusted to the components shown in Table 1 was prepared in a vacuum induction melting furnace, and powdered by gas atomization using N 2 gas. The temperature of the molten metal during gas atomization was in the range of liquidus temperature +50° C. to liquidus temperature +200° C. in order to lower the viscosity of the molten metal. The ratio of gas flow rate (m 3 /min)/melt flow rate (kg/min) during gas atomization was adjusted to 1.0 to 3.0 (m 3 /kg). Next, the obtained alloy powder was enclosed in a metal container, and ingots of test materials 1, 2 and 4 were produced by a known HIP treatment method.
- a molten metal having an iron-based alloy composition adjusted to the components shown in Table 1 was prepared in a vacuum induction melting furnace, and then the molten metal was transferred to a mold and solidified in the mold to produce an ingot. During this period, the same refractory used in normal operation was used for the tundish containing the molten metal and the refractory for the inner wall of the mold.
- Each obtained ingot is hot forged to produce a steel slab having a cross section of 80 mm x 80 mm, the steel slab is hot rolled to a thickness of 3.0 mm, and then cold rolled to a thickness of 0.30 mm. obtained a steel plate.
- the obtained steel sheet was subjected to so-called foil rolling (cold rolling, but called foil rolling to distinguish it from cold rolling after hot rolling) to produce an alloy foil (steel foil) having a thickness of 20 ⁇ m.
- foil rolling cold rolling, but called foil rolling to distinguish it from cold rolling after hot rolling
- the reduction ratio of each pass in cold rolling is 40 to 50%
- foil rolling each pass until the plate thickness is about 40 to 50 ⁇ m.
- the reduction rate of the passes was set to 20 to 50%, and then to 1 to 18% until the sheet thickness reached 20 ⁇ m. Annealing was performed as appropriate in order to remove strain due to cold rolling including foil rolling.
- test materials 1 to 4 were observed for inclusions on the surface of the metal foil using an SEM (JSM-IT500HR manufactured by JEOL Ltd.).
- SEM SEM
- the SEM settings are as follows. ⁇ Detector: Backscattered electron detector BED-C ⁇ Observation magnification: 80 times ⁇ Acceleration voltage: 20.0 kV ⁇ Working distance (WD): 10.0 mm ⁇ Irradiation current: 80%
- the image acquired by the SEM detects inclusions with inclusion automatic analysis software (AZtec particle analysis mode manufactured by Oxford), and the composition of inclusions is analyzed with an EDS device (ULTIM MAX 65 manufactured by Oxford). carried out.
- an SEM image used in the inclusion automatic analysis software is acquired.
- inclusions with an equivalent circle diameter of 2.00 ⁇ m or more were detected by inclusion automatic analysis software, and at least 1 element of Al, Mg, Si, Ca, Mn, and S was detected by EDS. Identify inclusions when more than one species is detected. Images for which EDS analysis has been completed are combined on software and output as one image. At that time, the grain size and elemental composition of inclusions identified by the inclusion automatic analysis software are also obtained.
- the evaluation area was 100 cm 2 , and the equivalent circle diameter was taken as the grain size of inclusions.
- the inclusions identified by the automatic analysis software for inclusions are calculated as oxides of Al 2 O 3 , MgO, SiO 2 , CaO, MnO, MnS, and CrS, and the content of the inclusions is The inclusion area ⁇ m 2 of each inclusion was obtained by multiplying the area of the inclusion obtained by the automatic analysis software. Next, all the inclusions were treated as described above, and the total area was determined for each oxide, and divided by the total area of all the inclusions to calculate the composition ratio of the inclusions.
- Tables 2 and 3 show the evaluation results of inclusions per 100 cm 2 for each metal mask material.
- Test materials 1 to 4 were cut into pieces of 100 mm ⁇ 100 mm, and etched (half-etched) to half the plate thickness with a mask hole pattern assuming a 1000 PPI OLED metal mask. After half-etching, the test materials 1 to 4 were evaluated for etching defects at 10 locations of 100 cm 2 and a total evaluation area of 1000 cm 2 . Further, pinholes were evaluated over the entire length of the metal foils (steel strips after rolling) of test materials 1 to 4, and the number of pinholes of ⁇ 20 ⁇ m or more was measured. Table 4 lists the results of etching defect evaluation and pinhole evaluation.
- Test material 2 has a larger total area ratio (ppm) of inclusions than test material 3.
- test materials 1 and 2 had inclusions with grain sizes in the range of 2.00 ⁇ m or more and 5.00 ⁇ m or less, that is, the proportion of inclusions within the size range that does not adversely affect etching There are many.
- the number density of inclusions having a size that may adversely affect etching that is, the number density of inclusions having a grain size of more than 5.00 ⁇ m is much lower than in test material 3.
- the average composition of inclusions having a particle size of 2.00 ⁇ m or more contained in test material 3 contains more than 30% by mass of Al 2 O 3 and more than 15% by mass of MgO. Therefore, it can be seen that there are many alumina and spinel as inclusions.
- the MgO content was suppressed to about 7.0% and the Al 2 O 3 content was 20.0% or less. Therefore, it can be seen that in test materials 1, 2 and 4, alumina and spinel are extremely reduced.
- Table 4 it can be seen that the etchability of test materials 1, 2 and 4, the number of pinholes, and the like are remarkably improved.
- an iron-based alloy foil in which coarse inclusions are reduced and defects are less likely to occur during rolling and etching. It is useful for downsizing or weight reduction, and can be suitably used for manufacturing OLEDs with high definition and resolution.
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Abstract
Description
多くの場合、電子部品のダウンサイジング化に伴い高精度化が必要になる。例えば、フォトエッチングは、電子部品の高精度加工に多用される技術であって、これを利用した電子部品の高精度化の例として、メタルマスクのマスク孔の微細化によるOLED(有機発光ダイオード)の高画素密度化やハードディスクドライブ(HDD)用のサスペンションの微細化等を挙げることができる。それに用いられるメタルマスクは、薄い金属板の表面にフォトレジスト法によるパターンを形成した後、エッチングによって金属板を溶解して製造される。
そして、反対側表面でドライフィルムが配置された部分も溶解され、反対側のドライフィルムが剥離する。そして、反対側から金属板をハーフエッチングした時に、ドライフィルムが剥離した部分の金属板もエッチングされることになり、介在物を中心として不定形の孔が空いた状態になる。
特許文献2は、溶湯の酸素濃度を低減するために、真空誘導溶解などにより溶湯の清浄度を高めてからインゴットを鋳造することによって、メタルマスク材料のエッチング不良を防止することを開示している。
さらに、連続鋳造の場合、タンディッシュ内の溶融スラグを除去しても、溶湯内に残存するアルミナ及びスピネルは界面エネルギーが高いので、溶湯の冷却中にクラスター化して粗大な介在物になりやすい。
(1)
質量%にて、
C:0.150%以下、
Si:2.00%以下、
Mn:10.00%以下、
Ni:2.00~50.00%、
Cr:19.00%以下、
N:0.20%以下、
Al:0.030%以下、
Co:5.00%以下、
Mg:0.0005%以下、
Ca:0.0005%以下、
Ti:0.01%以下、
P:0.035%以下、
S:0.0300%以下を含み、
残部がFe及び不純物からなる組成を有し、
粒径2.00μm以上の介在物の合計質量に対して、Al2O3:30質量%以下、MgO:15質量%以下であり、
前記粒径2.00μm以上の介在物のうち、粒径5.00μm以下の介在物の個数割合が80.00%以上であり、
板厚が10.00~30.00μmであることを特徴とする鉄系合金箔。
(2)
前記鉄系合金箔において、質量%にて、
Ni:30.00~50.00%であることを特徴とする(1)に記載の鉄系合金箔。
(3)
前記鉄系合金箔において、質量%にて、
C:0.050%以下、
Ca:0.0005%以下、
Mn:0.30%以下、
Si:0.30%以下、
Mg:0.0005%以下、
Al:0.030%以下のうち少なくとも1種を満足することを特徴とする(1)又は(2)に記載の鉄系合金箔。
(4)
粒径5.00μm超の介在物が15個/cm2以下であることを特徴とする(1)~(3)のいずれか一項に記載の鉄系合金箔。
(5)
前記鉄系合金箔の表面において、直径20μm以上のピンホール密度が5個/1000m2以下であることを特徴とする(1)~(4)のいずれか一項に記載の鉄系合金箔。
(6)
前記鉄系合金箔が、質量%にて、
C:0.150%以下、
Si:0.1~2.00%、
Mn:0.10~1.20%、
S:0.007%以下、
Ni:2.00~15.00%、
Cr:15.00~19.00%、
N:0.20%以下、
Al:0.010%以下を含み、
残部がFe及び不純物からなるオーステナイト系ステンレス鋼であって、表面において直径20μm以上のピンホール密度が5個/1000m2以下であって、0.2%耐力が700MPa以上であることを特徴とする(1)に記載の鉄系合金箔。
(7)
前記2.00μm以上の介在物が、表面において面積率で1~100ppmであることを特徴とする(6)に記載の鉄系合金箔。
(8)
(1)~(7)のいずれか一項に記載の鉄系合金箔からなるメタルマスク材料。
(9)
(1)~(7)のいずれか一項に記載の鉄系合金箔からなるメタルマスク。
(10)
(1)~(7)のいずれか一項に記載の鉄系合金箔を有する部品。
(11)
(1)~(7)のいずれか一項に記載の鉄系合金箔からなるハードディスクドライブサスペンション。
(12)
(10)に記載の部品が用いられた電子デバイス封止部材。
(13)
(1)~(3)、(6)のうちいずれかに記載の組成からなる鋼片を熱間圧延する工程と、
前記熱間圧延された熱延板を、仕上圧延を含む冷間圧延する工程とを含み、
前記冷間圧延における圧下率を99.0%以上とし、前記仕上圧延における各圧延パス(以下、単にパスと言う場合がある。)の圧下率を1~18%にすることを特徴とする鉄系合金箔の製造方法。
本発明の鉄系合金箔は、質量%にて、C:0.150%以下、Si:2.00%以下、Mn:10.00%以下、Ni:2.00~50.00%、Cr:19.00%以下、N:0.20%以下、Al:0.030%以下、Co:5.00%以下、Mg:0.0005%以下、Ca:0.0005%以下、Ti:0.01%以下、P:0.035%以下、S:0.0300%以下、残部がFe及び不純物からなる組成を有する。
しかしながら、Niは高価な元素であり、含有量が高過ぎれば、熱間圧延後又は熱間鍛造後において、鋼中にベイナイト組織が生成しやすくなる。従って、Ni含有量は50.00%以下、45.00%以下、40.00%以下、38.00%以下、又は37.00%以下とすることが好ましい。
Mnは含まなくてもよい。しかし、Mn含有量が少な過ぎると介在物をMn(O,S)-SiO2系の組成に調節することが困難になる。そのためMn含有量は、好ましくは0.01%以上、0.03%以上、0.05%以上、又は0.10%以上にするとよい。
ここで、Mn(O,S)とは、MnO単体、MnS単体、及びMnOとMnSが複合した介在物のことを指し、OとSの比率は一定ではなく、酸化物と硫化物が複合した介在物のことを意味する。
Siは含まなくてもよい。しかし、少な過ぎると脱酸不足となり、介在物中のCr2O3濃度が増加して、加工割れを誘発させる介在物が生成し易くなる。そこで、Si含有量は、好ましくは0.01%以上、0.03%以上、0.05%以上、又は0.10%以上にするとよい。
介在物は少ない方がよく、全く存在しないことが理想的である。しかし、製造過程で混入したり、鋼成分から生成したりするため、皆無にすることは容易ではない。前述したように、メタルマスクなどの素材として使用する場合、板厚の半分程度の大きさの介在物がエッチング不良の原因となり有害である。さらに、圧延中に表面にある粗大介在物が脱落し、ピンホールや表面ピットの原因となり易いことも分かった。従って、粒径の大きな介在物、例えば板厚10μmの極薄合金箔の場合、円相当粒径で5μm以上の介在物を極力低減させることが重要である。
介在物を混入させないためにはプロセスの見直しが重要になる。例えば、溶湯処理する際の耐火物を見直し、AlやMgなどが少ない耐火物を使用するとよい。
さらに、介在物の凝集は、例えば溶湯から凝固する際の偏析し凝集することが原因の一つである。凝固の際に偏析することは避けることは容易ではないが、できるだけ凝集しないよう溶湯を攪拌させるなどの方法が考えられる。さらに、溶湯からの凝固プロセスを使用しないプロセス、例えばHIP(熱間静水圧プレス)などによりインゴットを製造するとよい。製造プロセスについては後で説明する。
・検出器: 反射電子検出器BED-C
・観察倍率: 80倍
・加速電圧: 20.0 kV
・ワーキングディスタンス(WD): 10.0 mm
・照射電流: 80%
また、SEMで取得した画像は介在物自動解析ソフトにて介在物を検出し、エネルギー分散型X線分光装置(以下、EDS装置)にて介在物の組成分析を実施した。介在物自動解析のソフトウェアに関しては、例えばOxford社製のAZtecの粒子解析モードを使用してもよい。EDS装置は、例えばOxford社製のULTIM MAX 65を用いてもよい。
介在物自動解析ソフトによる介在物の識別工程において、初めに介在物自動解析ソフトで使用するSEM像を取得する。次にSEMで取得した画像から介在物自動解析ソフトにて円相当直径(等面積円相当直径)で2.00 μm以上であり、かつEDSでAl、Mg、Si、Ca、Mn、Sの元素のうち一種以上が検出された場合に介在物として識別する。EDS分析まで終わった画像についてはソフト上で結合し、1つの画像として出力する。その際、介在物自動解析ソフトにより識別された介在物の円相当直径、元素組成も取得する。以上の介在物識別の手順を繰り返し実施することで設定した面積まで測定を行う。例えば、画像の測定面積は10cm2を測定の単位である1視野とし、10視野測定を実施し、合計100cm2を評価面積とするとよい。なお、測定した介在物の面積と同じ面積を持つ円の直径を円相当径(円相当直径)とし、これを「粒径」とする。
Mn、Crは主として硫化物で存在し、Mnは酸化物MnOとしても存在することもある。Sは前述の硫化物MnS以外に、クロムの硫化物CrSとして存在することもある。Mnのみかけの物質量よりSのみかけの物質量が多い場合、Mnのみかけの物質量と同量のMnSが存在し、このとき、Sのみかけの物質量からMnのみかけの物質量を減算した物質量のCrSが存在する。Mnのみかけの物質量よりSのみかけの物質量が少ない場合、Sのみかけの物質量と同量のMnSが存在し、このときMnのみかけの物質量からSのみかけの物質量を減算した物質量のMnOが存在する。Mnのみかけの物質量とSのみかけの物質量が全く同量存在する場合、Mn及びSの物質量と同量のMnSが存在する。
介在物の基本成分である酸化物あるいは硫化物の状態にするため、各元素のみかけの物質量に対応する元素O(酸素)又はSの物質量をそれぞれAl:O=2:3、Mg:O=1:1、Si:O=1:2、 Ca:O=1:1、Mn:O=1:1、Mn:S=1:1、S:Cr=1:1の量論比に基づき付与した後、それぞれの分子量をかけて酸化物等換算質量を導出する。求めた酸化物等換算質量のそれぞれを、7つの酸化物等換算質量の合計で割ることで、Al2O3、MgO、SiO2、CaO、MnO、MnS、CrS(以下、「酸化物等」と言う場合がある。)の酸化物等換算質量%を求める。介在物自動解析ソフトで求めた介在物の面積に対し、7つの酸化物等換算質量%をそれぞれ積算し、Al2O3、MgO、SiO2、CaO、MnO、MnS、CrSの介在物面積μm2を求める。
次に、介在物自動解析ソフトで識別された全介在物について介在物面積をそれぞれ求め、上記7つの酸化物あるいは硫化物毎に介在物面積を合計して、Al2O3の面積合計、MgOの面積合計、SiO2の面積合計、CaOの面積合計、MnOの面積合計、MnSの面積合計、CrSの面積合計を得る。この7つの面積合計の総和を全介在物の面積合計とする。各酸化物等の面積合計を全介在物の面積合計で割ることで、介在物の組成比率(質量%)を算出する。
介在物の面積率は、各酸化物等の面積の合計、あるいは、全介在物の面積合計を評価面積で割り、各酸化物等それぞれの面積率、あるいは、全介在物の面積率とする。
なお、金属箔中で介在物が不均一に存在する場合、SEMで観察する箇所により介在物の存在状況が変わりうると考えられる。そこで、以下の方法により評価面積の妥当性を検証した。まず、200 cm2のSEM測定を行い、介在物自動解析ソフトにより介在物を識別した。この測定面積を格子状に200個に等分する。この時1つの格子は1辺1cmの正方形であり、その面積は1cm2となるようにする。次に、統計数を増やすため200個の格子からランダムにk個選び、仮想的に1cm2×k個=kcm2測定した時の全介在物の個数密度を導出し、これを1000回繰り返し、測定面積がkcm2の時の個数密度を1000個得た。ここで、全介在物個数密度は、測定面積kcm2において観測された全介在物の個数を測定面積で割ることにより導出し、kはそれぞれ1、2、4、5、8、10、20、25、40、50、100、200とした。次に、k=200cm2における全介在物の個数密度を図1のaverage(実線)で表し、得られた1000個の個数密度の最大値及び最小値を図1のエラーバーとして示した。図1より、評価面積100cm2であればaverage±10%以内に収まっていることを検証した。この結果から、好ましい評価面積は100cm2であると考え、前記評価面積を100cm2と決定した。
前述したように軟質系介在物は圧延過程において展伸、破砕して微細化し、5.00μm以上の粗大粒を低減することができる。このため鉄系合金箔の圧延過程において圧下率を高くするとよい。そのため、鉄系合金箔の板厚は特に限定しないものの、通常の製造工程においてインゴット(鋳塊)の大きさはある程度必要なため、板厚は30.00μm以下にすることが好ましい。好ましくは27.50μm以下、25.00μm以下、又は22.50μm以下にするとよい。一方、板厚が10.00μm未満の場合、エッチング加工時又は圧延加工時に取り扱いの難易度が増すため、皺などの欠陥が生じるおそれがあるため板厚は10.00μm以上にするとよい。
粗大介在物が合金箔の表面に存在していると、圧延時などに脱落し、その部分に凹部となる。そのまま、圧延すると凹部が拡大し、円相当径で20μm(φ20μm)程度以上のピンホールとなる。本発明に係る鉄系合金箔は、粗大介在物が減少するため、粗大介在物の脱落に起因するピンホールも減少し、φ20μm以上のピンホールを5個/1000m2以下にすることができる。
上記に規定した組成であれば、0.2%耐力を700MPa以上にすることができる。700MPa以上の0.2%耐力がれば、通常の使用条件下で曲げ癖が付かずにメタルマスクなどに適用することができる。
本発明に係る鉄系合金箔は、例えば、次のように製造することができる。以下に示す方法は例示であって、これに限定されることを意図しない。
そのため、ガス流量と溶湯流量の比は0.3(m3/kg)以上、好ましくは0.5以上、0.7以上、0.9以上、1.0以上、1.5以上、又は2.0以上とすることが好ましい。ガス流量(m3/分)/溶湯流量(kg/分)の比の上限は特に限定しないが、5.0(m3/kg)以上では冷却能力が飽和するので、上限は、5.0(m3/kg)にするとよい。
即ち、冷間圧延において総圧下率を97.0%以上にし、仕上圧延前の冷間圧延では圧下率を20%以上として軟質介在物を微細化し、仕上圧延ではマイルド圧延にして介在物の脱落を抑制するとよい。
一般に、最終板厚の10倍程度の板厚から最終板厚までの圧延(冷間圧延)を箔圧延と呼び、熱延後の冷間圧延と区別する場合がある。この場合、熱延後の冷間圧延、それに続く箔圧延のうち仕上圧延前までの圧延、そして最終の仕上圧延の順に圧下率を下げていくとさらによい。例えば、各パスの圧下率を、熱延後の冷間圧延は40%以上とし、仕上圧延前の箔圧延は20%以上とし、箔圧延のうち仕上圧延は20%未満にするとよい。
ここで、圧下率とは、圧延前の板厚をt1、圧延後の板厚をt2とした時に、以下の式で示される。
圧下率=(t1-t2)/t1
例えば仕上圧延が多段圧延であっても、その累積圧下率は、仕上圧延前の板厚をt1、仕上圧延後の板厚をt2として算出すればよい。各パスの圧下率は、各圧延パス前の板厚をt1、当該圧延パス後の板厚をt2として算出すればよい。
即ち、質量%にて、C:0.150%以下、Si:0.1~2.00%、Mn:0.10~1.20%、S:0.007%以下、Ni:2.00~15.00%、Cr:15.00~19.00%、N:0.20%以下、Al:0.010%以下を含み、残部がFe及び不純物からなるオーステナイト系ステンレス鋼。
この場合も、上記の説明と同様、アルミナやスピネル系の介在物を低減することができ、エッチング性がよく、高精度加工性に優れた合金箔を得ることができる。
試験材1、2、4については、真空誘導溶解炉により表1に示す成分に調整した鉄系合金組成の溶湯を調製し、N2ガスによるガスアトマイズにより粉末化した。ガスアトマイズ時の溶湯温度は、溶湯の粘性を下げるために、液相線温度+50℃~液相線温度+200℃の範囲とした。また、ガスアトマイズ時のガス流量(m3/分)/溶湯流量(kg/分)の比は1.0~3.0(m3/kg)になるよう調整した。
次に、得られた合金粉末を金属容器に封入し、公知のHIP処理方法により試験材1、2、4のインゴットを製造した。
試験材3も真空誘導溶解炉により表1に示す成分に調整した鉄系合金組成の溶湯を調製したが、その後溶湯を鋳型に移し、鋳型中で凝固させインゴットを製造した。この間、溶湯を入れたタンディッシュや鋳型内壁の耐火物は、通常操業で使用するものと同等の耐火物を使用した。
得られた各インゴットを熱間鍛造して断面が80mm×80mmの鋼片を製造し、当該鋼片を3.0mm厚になるまで熱間圧延し、その後冷間圧延して板厚0.30mmの鋼鈑を得た。得られた鋼鈑をいわゆる箔圧延(冷間圧延であるが、熱延後の冷間圧延と区別して箔圧延と呼ぶ。)して、板厚20μmの合金箔(鋼箔)を製造した。この時、狙いの板厚に造り込む最終圧延や形状矯正圧延を除き、冷間圧延での各パスの圧下率を40~50%に、箔圧延において板厚40~50μm程度になるまでの各パスの圧下率を20~50%に、その後板厚20μmになるまでを1~18%にした。なお、箔圧延を含む冷間圧延による歪除去のため適宜焼鈍を行った。
・検出器: 反射電子検出器BED-C
・観察倍率: 80倍
・加速電圧: 20.0 kV
・ワーキングディスタンス(WD): 10.0 mm
・照射電流: 80%
また、SEMで取得した画像は介在物自動解析ソフト(Oxford社製のAZtecの粒子解析モード)にて介在物を検出し、EDS装置(Oxford社製のULTIM MAX 65)にて介在物の組成分析を実施した。
介在物の組成は、前記介在物自動解析ソフトで識別された介在物についてAl2O3、MgO、SiO2、CaO、MnO、MnS、CrSの酸化物等換算質量%を計算し、前記介在物自動解析ソフトで求めた介在物の面積を乗算して各介在物の介在物面積μm2を求めた。次に、全介在物について前記の処理を行い酸化物毎に面積合計を求め、全介在物の面積合計で割り、介在物の組成比率を算出した。
試験材1~4を100mm×100mmに切断し、1000PPIのOLEDメタルマスクを想定したマスク孔パターンで板厚の半分までエッチング(ハーフエッチング)した。ハーフエッチング後の試験材1~4について、100cm2で10か所、合計評価面積1000cm2でエッチング不良を評価した。また、ピンホールに関しては試験材1~4の金属箔(圧延後の鋼帯)の全長に亘り評価し、φ20μm以上のピンホール数を測定した。エッチング不良評価とピンホール評価の結果を表4に記載する。
その結果、表4に示すように、試験材1,2及び4のエッチング性、ピンホール数などが著しく改善されていることが分かる。
Claims (13)
- 質量%にて、
C:0.150%以下、
Si:2.00%以下、
Mn:10.00%以下、
Ni:2.00~50.00%、
Cr:19.00%以下、
N:0.20%以下、
Al:0.030%以下、
Co:5.00%以下、
Mg:0.0005%以下、
Ca:0.0005%以下、
Ti:0.01%以下、
P:0.035%以下、
S:0.0300%以下を含み、
残部がFe及び不純物からなる組成を有し、
粒径2.00μm以上の介在物の合計質量に対して、Al2O3:30質量%以下、MgO:15質量%以下であり、
前記粒径2.00μm以上の介在物のうち、粒径5.00μm以下の介在物の個数割合が80.00%以上であり、
板厚が10.00~30.00μmであることを特徴とする鉄系合金箔。 - 前記鉄系合金箔において、質量%にて、
Ni:30.00~50.00%
であることを特徴とする請求項1に記載の鉄系合金箔。 - 前記鉄系合金箔において、質量%にて、
C:0.050%以下、
Ca:0.0005%以下、
Mn:0.30%以下、
Si:0.30%以下、
Mg:0.0005%以下、
Al:0.030%以下のうち
少なくとも1種を満足することを特徴とする請求項1又は2に記載の鉄系合金箔。 - 粒径5.00μm超の介在物が15個/cm2以下であることを特徴とする請求項1~3のいずれか一項に記載の鉄系合金箔。
- 前記鉄系合金箔の表面において、直径20μm以上のピンホール密度が5個/1000m2以下であることを特徴とする請求項1~4のいずれか一項に記載の鉄系合金箔。
- 前記鉄系合金箔が、質量%にて、
C:0.150%以下、
Si:0.1~2.00%、
Mn:0.10~1.20%、
S:0.007%以下、
Ni:2.00~15.00%、
Cr:15.00~19.00%、
N:0.20%以下、
Al:0.010%以下を含み、
残部がFe及び不純物からなるオーステナイト系ステンレス鋼であって、
表面において直径20μm以上のピンホール密度が5個/1000m2以下であって、
0.2%耐力が700MPa以上であることを特徴とする請求項1に記載の鉄系合金箔。 - 前記2.00μm以上の介在物が、表面において面積率で1~100ppmであることを特徴とする請求項6に記載の鉄系合金箔。
- 請求項1~7のいずれか一項に記載の鉄系合金箔からなるメタルマスク材料。
- 請求項1~7のいずれか一項に記載の鉄系合金箔からなるメタルマスク。
- 請求項1~7のいずれか一項に記載の鉄系合金箔を有する部品。
- 請求項1~7のいずれか一項に記載の鉄系合金箔からなるハードディスクドライブサスペンション。
- 請求項10に記載の部品が用いられた電子デバイス封止部材。
- 請求項1~3及び6のいずれか一項に記載の組成からなる鋼片を熱間圧延する工程と、 前記熱間圧延された熱延板を、仕上圧延を含む冷間圧延する工程とを含み、
前記冷間圧延における圧下率を99.0%以上とし、
前記仕上圧延における各パスの圧下率を1~18%にすることを特徴とする鉄系合金箔の製造方法。
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