CN107075688B - Hot rolling titanium slab and its manufacturing method - Google Patents
Hot rolling titanium slab and its manufacturing method Download PDFInfo
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- CN107075688B CN107075688B CN201480082171.1A CN201480082171A CN107075688B CN 107075688 B CN107075688 B CN 107075688B CN 201480082171 A CN201480082171 A CN 201480082171A CN 107075688 B CN107075688 B CN 107075688B
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- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 89
- 239000010936 titanium Substances 0.000 title claims abstract description 87
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 86
- 238000005098 hot rolling Methods 0.000 title claims description 56
- 238000004519 manufacturing process Methods 0.000 title claims description 32
- 230000000087 stabilizing effect Effects 0.000 claims abstract description 116
- 238000002844 melting Methods 0.000 claims abstract description 83
- 230000008018 melting Effects 0.000 claims abstract description 83
- 238000007711 solidification Methods 0.000 claims abstract description 67
- 230000008023 solidification Effects 0.000 claims abstract description 67
- 239000000463 material Substances 0.000 claims abstract description 52
- 238000010438 heat treatment Methods 0.000 claims abstract description 31
- 238000010894 electron beam technology Methods 0.000 claims abstract description 29
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 24
- 239000002994 raw material Substances 0.000 claims abstract description 23
- 238000005096 rolling process Methods 0.000 claims abstract description 23
- 239000012634 fragment Substances 0.000 claims abstract description 22
- 239000000843 powder Substances 0.000 claims abstract description 16
- 239000011888 foil Substances 0.000 claims abstract description 12
- 239000000155 melt Substances 0.000 claims description 10
- 230000008859 change Effects 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 230000007935 neutral effect Effects 0.000 claims description 5
- 239000010410 layer Substances 0.000 abstract description 74
- 238000000034 method Methods 0.000 abstract description 48
- 239000002344 surface layer Substances 0.000 abstract description 39
- 230000008569 process Effects 0.000 abstract description 34
- 238000003723 Smelting Methods 0.000 abstract description 8
- -1 line Substances 0.000 abstract description 2
- 238000005266 casting Methods 0.000 description 61
- 238000005520 cutting process Methods 0.000 description 30
- 238000005554 pickling Methods 0.000 description 27
- 230000000052 comparative effect Effects 0.000 description 13
- 230000004927 fusion Effects 0.000 description 10
- 239000000956 alloy Substances 0.000 description 9
- 239000000523 sample Substances 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 8
- 238000004458 analytical method Methods 0.000 description 8
- 239000013078 crystal Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000010891 electric arc Methods 0.000 description 7
- 229910052758 niobium Inorganic materials 0.000 description 7
- 229910052720 vanadium Inorganic materials 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 229910052804 chromium Inorganic materials 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- 229910052715 tantalum Inorganic materials 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 239000002699 waste material Substances 0.000 description 5
- 238000005242 forging Methods 0.000 description 4
- 239000004615 ingredient Substances 0.000 description 4
- 150000002500 ions Chemical class 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 230000035515 penetration Effects 0.000 description 4
- 238000005480 shot peening Methods 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 239000008187 granular material Substances 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 229910001040 Beta-titanium Inorganic materials 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- 230000005611 electricity Effects 0.000 description 2
- 238000001493 electron microscopy Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 238000004093 laser heating Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000002798 spectrophotometry method Methods 0.000 description 2
- 238000005406 washing Methods 0.000 description 2
- 102100024768 ATP-dependent RNA helicase DDX50 Human genes 0.000 description 1
- 101710156103 ATP-dependent RNA helicase DDX50 Proteins 0.000 description 1
- 229910011214 Ti—Mo Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000013507 mapping Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052763 palladium Inorganic materials 0.000 description 1
- 230000000149 penetrating effect Effects 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229910052707 ruthenium Inorganic materials 0.000 description 1
- 238000001304 sample melting Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/06—Casting non-ferrous metals with a high melting point, e.g. metallic carbides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D29/00—Removing castings from moulds, not restricted to casting processes covered by a single main group; Removing cores; Handling ingots
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
- C23C26/00—Coating not provided for in groups C23C2/00 - C23C24/00
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Metal Rolling (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Continuous Casting (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
At the surface as rolling surface of the titanium slab comprising titanium alloy manufactured using electron-beam process, plasma arc smelting process, there is melting solidification layer again in range more than depth 1mm, the melting is obtained from solidification layer is the one or two or more kinds of β phase stabilizing element of addition and makes its melting and solidify again again, until depth 1mm in the range of concentration of the average value in terms of quality % than the β phase stabilizing element in base material of concentration of β phase stabilizing element be higher by 0.08 mass % or more and 1.50 mass % or less.As the raw material containing β phase stabilizing element, powder, fragment, line, foil are used.In addition, being heated as the means for melting surface layer using electron beam heating and plasma arc.
Description
Technical field
The present invention relates to the manufacturing methods of titanium slab of the hot rolling comprising titanium alloy, though more particularly to omit breaking down,
The coggings processes such as forging can also keep the titanium slab and its manufacturing method of the surface texture after hot rolling well.
Background technique
Titanium material is molten using non-consumable electrode formula arc melting method, electron beam usually using titanium sponge, titanium waste material as raw material
Refining method, plasma arc smelting process etc. carry out melting, to form titanium ingot casting (titanium slab).On-consumable formula arc melting method
In, using briquet obtained from titanium sponge press molding as electrode, so that electrode and mold is carried out arc discharge, make electrode itself
It melts, and is cast in mold, to obtain ingot casting.Therefore, it is necessary to the electric discharge of mold and electrode is equably carried out, thus
Mold shape is set to be defined as cylinder type, the ingot casting shape after casting becomes cylindric.On the other hand, electron-beam process, etc.
Electron beam and plasma arc are used in gas ions arc melting method respectively, it, will be in melting although smelting process is different
The titanium melt of melting on siege is injected into mold, therefore, the selection of mold shape be it is free, be not limited to it is cylindric, can be with
Manufacture the ingot castings of various shapes such as rectangle, steel billet shape.
In current titanium material manufacturing process, passing through the heat such as breaking down, the forging for being referred to as cogging process of ingot casting later
After manufacturing procedure, implement hot rolling, cogging process is required.It is believed that utilizing rectangle ingot casting (slab from its shape
Shape ingot casting) manufacture plate when can be omitted cogging process, can be saved when using cylindric and steel billet shape ingot casting manufacture bar, wire rod
Slightly cogging process has studied carry out hot rolling technology with omitting cogging process.If establishing the technology, can expect to pass through province
Slightly process improves cost with yield rate is improved.
However, when the titanium slab manufactured using electron-beam process, plasma arc smelting process is due to maintaining casting
State, therefore exist and reach the coarse granule of tens of mm.For such titanium slab, when carrying out hot rolling with omitting cogging process,
As, with the influence of each intercrystalline ANISOTROPIC DEFORMATION, generating bumps in the crystal grain as caused by coarse granule on surface, becoming
Surface blemish.In order to remove the surface blemish generated in hot rolling, it is necessary to increase heat using as the pickling process of subsequent handling
The molten amount of cutting on rolled material surface, yield rate correspondingly deteriorate, and worry increased costs.
Therefore, for the titanium ingot casting manufactured using electron-beam process, plasma arc smelting process, on the one hand expect logical
The coggings such as omission breaking down, forging process is crossed to improve cost, on the other hand worries to cause cost to increase because of the increase of surface blemish
Add, hampers the functionization for omitting the titanium slab of cogging process.
Following method is disclosed in patent document 1: being carried out melting in electron beam furnace, is directly taken out out of mold
In the section structure of titanium plate base, from surface layer towards the casting direction angulation θ of internal solidification direction and slab for 45 °~
In the case where 90 °, or in the crystal orientation distribution on surface layer, the c-axis of hcp is with the normal angulation on slab surface layer
In the case where 35 °~90 °, cast(ing) surface is good, and even if omit ingot casting cogging process can improve hot rolling after surface
Flaw.That is, being able to suppress the flaw generated by this coarse grain by the grain shape on control surface, crystal orientation.
In patent document 2, the method for cogging process and directly progress hot rolling as the ingot casting for omitting titanium material passes through benefit
With high-frequency induction heating, electric arc heated, plasma heating, electron beam heating and laser heating etc., the table of rolling surface is become
The surface layer in face is melted and is solidified again, to carry out grain refined 1mm or more deep from surface layer.By utilizing the slab surface layer
Quenching solidification and form the distribution of fine and irregular crystal orientation, to prevent the generation of surface blemish.
Existing technical literature
Patent document
Patent document 1: No. 2010/090353 bulletin of International Publication
Patent document 2: Japanese Unexamined Patent Publication 2007-332420 bulletin
Summary of the invention
Problems to be solved by the invention
The present invention provides: although omit cogging process and do not need to the titanium blank surface of state when maintaining casting into
The process of row cutting finishing, the titanium after still can inhibit subsequent hot rolling generate titanium slab and its manufacturer of surface blemish
Method.
The solution to the problem
The inventors of the present invention have made intensive studies to realize aforementioned problems.Itself as a result, it has been found that, as titanium alloy titanium
The method of smelting of slab, for shape when maintaining casting using electron-beam process, the manufacture of plasma arc smelting process
For the titanium slab of state, when carrying out hot rolling with omitting the cogging process needed in the past, as the preceding process of hot rolling, casting is being maintained
The rolling surface surface layer of the titanium slab of state when making be arranged or spread containing β phase stabilizing element raw material (powder, fragment,
Line, foil), the surface layer of titanium is melted together with raw material.In this way, forming the concentration of β phase stabilizing element on titanium surface layer
Layer, the i.e. β phase stabilizing element enriched layer higher than base material.It can keep the surface texture after hot rolling well as a result,.
That is, the present invention is as described below.
(1) a kind of titanium slab, which is characterized in that it is the titanium slab comprising titanium alloy,
At the surface for becoming rolling surface, have in the range more than depth 1mm comprising one or two or more kinds of β phases
The layer of stabilizing element,
The average value of the concentration of β phase stabilizing element in the range of until depth 1mm is in terms of quality % than in base material
The concentration of β phase stabilizing element be higher by 0.08 mass % or more and 1.50 mass % or less.
(2) the titanium slab according to (1), wherein aforementioned β phase stabilizing element is one of Fe, Ni, Cr or two kinds
More than.
(3) the titanium slab according to (1), wherein while containing aforementioned β phase stabilizing element, also containing one kind
Or two kinds or more of α phase stabilizing element or neutral element.
(4) a kind of manufacturing method of titanium slab, wherein make the titanium slab comprising titanium alloy surface as rolling surface and
After raw material containing β phase stabilizing element melt together, make its solidification, the β phase in the range of making until depth 1mm is stable
Change concentration of the average value of the concentration of element in terms of quality % than the β phase stabilizing element in base material and is higher by 0.08 mass % or more
And 1.50 below mass %.
(5) manufacturing method of the titanium slab according to (4), wherein the aforementioned raw material containing β phase stabilizing element are
Powder, fragment, line, any form in foil.
(6) manufacturing method of the titanium slab according to (4), wherein using electron beam heating or plasma heating, make
The melt surface as rolling surface of the aforementioned titanium slab comprising titanium alloy.
The effect of invention
For titanium slab of the invention, even if omit the coggings works such as breaking down (slabbing step), the forging needed in the past
Implement hot rolling to sequence (breakdown step), can also manufacture the titanium with the surface texture being equal with current material.It can
To reduce heating time by omitting cogging process, be smoothed concomitantly by the surface layer for melting bring titanium slab with surface layer
It reduces cutting finishing, molten amount of cutting when pickling etc. is reduced by the raising of the titanium surface texture after hot rolling, thus bring into
The raising of product rate, therefore be effective, in its inestimable industry effect to the reduction of manufacturing cost.
Detailed description of the invention
Fig. 1 shows the schematic diagram for melting again the concentration variation of solidification layer.
Specific embodiment
Hereinafter, the present invention is described in detail.
In general, titanium alloy is to manufacture into the shapes such as plate, wire rod or bar by progress hot rolling, cold rolling.The present invention
In, titanium alloy refers to, alpha titanium alloy and alpha and beta titanium alloy.
In the present invention as the titanium slab of object be rectangle ingot casting (slab shape ingot casting), cylindrical ingot, steel billet shape ingot casting.
For following technology: melting the surface layer of the titanium slab of these shapes together with the raw material containing β phase stabilizing element to right
Titanium after hot rolling inhibits surface blemish.
In the present invention, only the surface section of the titanium slab of state when maintaining casting is heated, depth 1mm or more is molten
Melt.For the surface section of the titanium slab so by melting, when carrying out quenching after melting and solidifying and be cooled to room temperature again
Melting again solidification layer (will so by only by the heating of the surface section of the titanium slab of state when maintaining casting and make its melting,
Be quenched later and the solidification layer that solidifies again be known as " melting again solidification layer ") section structure become fine acicular structure or
Person's martensitic structure.Moreover, by melting base material and β phase stabilizing element simultaneously when surface layer melts, thus compared with base material,
The β phase stabilizing element concentration melted in solidification layer again is got higher, as a result, due to adding the bring through hardening of β phase stabilizing element
Property improve, and the phase transformation of α phase or martensitic traoformation are carried out in cooling, so as to so that melting again solidification layer formed it is finer
Tissue.So-called herein " harden ability raising " refers to, β phase stabilizing element is contained in the surface layer by making titanium slab, to make to connect
Transformation temperature (nose) when continuous cooling is displaced to long-time side, so that it is carried out the phase transformation of α phase at low temperature or is made its progress
Martensitic traoformation.Purpose is, miniaturize crystal grain to increase karyogenesis site by making it carry out phase transformation at low temperature.
Further, titanium slab that above-mentioned melting solidifies again has been carried out since the β phase degree of stabilisation melted in solidification layer again becomes
Thus height, therefore melting becomes the state of two phase region of alpha+beta in solidification layer again when hot rolling is heated, there are α phase and β phase this 2 phases,
Grain growth is suppressed, the hot rolling after the fine-grain holding fine-particle state after melting being solidified again hot rolling being maintained to heat
When.Thus, it can be known that the bumps on the titanium surface caused by can inhibiting by coarse grain, can manufacture and not generate surface blemish
Titanium hot rolling material.
Details is as be described hereinafter, and in the present invention, solidification layer generates deep part and shallow part again for the melting of formation.This hair
In bright, make the depth 1mm or more for melting again solidification layer, which refers to, in the side vertical with the scanning direction of fusion weld pearl
To section in observe when most superficial part depth.
The depth 1mm or more on the surface layer of titanium slab is carried out as described above it is remelted after, solidified, thus from surface layer
The depth risen is that 1mm or more becomes fine acicular structure or martensitic structure, due to melting solidification layer again and its heat affected zone,
Titanium plate thickness direction center side becomes the tissue of state when maintaining casting.It is a feature of the present invention that will at least be cast with titanium
After the surface layer that the rolling surface of base is in contact is remelted together with the raw material containing β phase stabilizing element, solidified, thus from
Melting the depth that the surface layer in solidification layer again is risen is the average value of the concentration of the β phase stabilizing element until 1mm than the β in base material
The concentration of phase stabilizing element is higher by a certain amount of.Even if being melted with not adding β stabilizing element and solidifying processing again, for containing
There is alpha and beta titanium alloy of the β phase stabilizing element as composition of alloy, also there is the crystal grain micronized effect for melting again solidification layer.So
And in the processing, is melted when solidifying processing again, for the composition of fusing department, surface layer is melted together with β phase stabilizing element
It when melting, will immediately begin to solidify after just melting, therefore will not fully cause to spread in fusing department, β phase stabilizes member
The inhomogeneities of plain concentration remains.When such inhomogeneities remains, the highly concentrated region of β phase stabilizing element is generated, is become
Finer tissue.In addition, even if tissue miniaturization is reached in melting when solidifying again, having in the case where keeping base material directly remelted
When also will form each crystal grain have same crystal orientation aggregate, i.e. colony.Such colony is due to crystalline substance having the same
Body orientation, therefore acted as coarse granule.Therefore, because the influence of ANISOTROPIC DEFORMATION and be possible to hot rolling flaw send out
Exhibition.However, in the case where the inhomogeneities with β phase stabilizing element concentration, as described above, due to β phase stabilizing element
Concentration difference and be formed locally fine-grain, so as to inhibit the colony generation, hot rolling heating when can inhibit colony
Growth.The average value of the concentration of β phase stabilizing element of the melting until the depth from surface layer in solidification layer is 1mm again with
Quality % meter is higher by 0.08 mass % or more and 1.50 mass % or less than the concentration of the β phase stabilizing element in base material.β
Phase stabilizing element can combine multiple β phase stabilizing elements and add, the concentration of β phase stabilizing element at this time refer to containing
β phase stabilizing element each concentration summation.Only by with base material and the concentration for melting again the β phase stabilizing element of solidification layer
Difference be 0.08 mass % or more mode add β stabilizing element, so that it may obtain effect, therefore as lower limit.For
Further to play the effect for inhibiting surface blemish, the concentration difference of β phase stabilizing element is preferably greater than 0.2 mass %, and then most
Preferably greater than 0.5 mass %.In addition, if the concentration difference of base material and the melting β phase stabilizing element of solidification layer again is in aforementioned model
In enclosing, then the process of hot rolling and subsequent process, i.e. shot-peening and pickling, the enriched layer quilt of the β phase stabilizing element on surface layer are utilized
It is innoxious to melt the β phase stabilizing element progress being enriched in solidification layer again for removal.That is, passing through the work for carrying out shot-peening and pickling
Sequence becomes the ingredient and machinery being equal with the cold-reduced sheet manufactured by common preparation method so that β phase stabilizing element enriched layer disappears
Characteristic.However, when base material is higher than 1.50 mass % with the concentration difference for melting again the β phase stabilizing element of solidification layer, titanium slab table
The ratio of β phase obviously aoxidized in layer increases, thus compared with base material, amount of oxidation is significantly increased and then titanium slab table when hot rolling
Solidification layer and the difference of thermal change form drag in base material become larger again for the melting of layer, crack sometimes in surface layer, above-mentioned boundary part
Deng.For these factors, it is necessary to increase the molten amount of cutting in surface in pickling process, yield rate is substantially reduced.In addition, subsequent handling
In, the innoxious of the enriched layer of β phase stabilizing element also becomes difficult, and therefore, the β phase until the depth from surface layer is 1mm is stable
The average value for changing the concentration of element is set as 1.50 mass % or less relative to the concentration of the β phase stabilizing element of base material.In addition, making
Fusion penetration is 1mm or more, if fusion penetration becomes too deep, has and stabilizes member with residual β phase after pickling process in shot-peening
The worry of the enriched layer of element, it is therefore desirable for until fusion penetration is 5mm or so.
In addition, in general, titanium slab rises in the titanium blank surface portion that is in contact of casting Shi Congyu mold is solidified, therefore it is logical
The solute distribution by element is crossed, the ingredient in the surface layer and inside of titanium slab only has micro difference.The β phase stabilizing element such as Fe
It is the element of normal segregation to be shown, therefore in solidification, when phase transformation, there is the Fe concentration of the surface section of titanium slab to be lower, titanium slab
The tendency that internal Fe concentration is got higher.Therefore, by melting β phase stabilizing element and base material simultaneously, so that melting be made to solidify again
It is extremely effective that β phase stabilizing element concentration in layer, which is base material or more,.The effect is particularly evident in alpha titanium alloy.
In addition, when casting titanium, by controlling the input amount of raw material, so as to adjust at the uniform shape of ingredient of slab entirety
State.However, part generates the variation etc. of ingredient sometimes.Therefore, for β stabilizing element concentration just low alloy originally,
In melting and solidification layer, there are the insufficient regions of fine-grainization corresponding with the composition variations of β stabilizing element, exist sometimes
Part real estate gives birth to surface blemish after hot rolling.Therefore, steady to improve β phase by adding β stabilizing element when melting solidifies again
Surely the additive amount for changing element is effectively, can also to inhibit the surface blemish locally generated as a result,.In addition, as described above, melting
Melt the composition variations of the β stabilizing element in solidifying phase for β stabilizing element concentration originally for high alloy, with base material
Composition variations compared to big, therefore the effect of disjunction colony also becomes much larger, and can also inhibit the surface blemish locally generated.
When from the cross-section observation in the direction vertical with the scanning direction of fusion weld pearl, there is the shape of melting solidification layer again in titanium
Fusion weld pearl center when blank surface is remelted becomes most deep tendency, when being overlapped fusion weld pearl, becomes in adjacent melting
The weldering mutual centre of pearl becomes most shallow, the form that most deep and most superficial part are repeated periodically.At this point, most deep and most superficial part it
When difference is big, difference is generated in terms of deformation drag because of the difference when hot rolling, leads to flaw due to its sometimes.Therefore, ideal
, above-mentioned difference is lower than 2mm.It should be noted that making the depth 1mm or more for melting again solidification layer in the present invention, the depth
Degree refers to, the depth of most superficial part when from the cross-section observation in the direction vertical with the scanning direction of fusion weld pearl.
To melting again the depth of solidification layer, melting solidify again in the measuring method of inhomogeneities be illustrated.Will from
It the part that the titanium blank surface portion in the section in the vertical direction in the scanning direction of fusion weld pearl is cut out, will as embedment grinding sample
It is supplied to SEM (Scaning Electron Microscopy)/EPMA (Electron Probe MicroAnalyser), by
This can easily judge.In the present invention, melting is solidified into the depth that layer depth is defined as most superficial part again, therefore reflect using element
It is easy for penetrating analysis and finding out fusion penetration.The one of base material and the measured value for the concentration variation for melting again solidification layer is shown in Fig. 1
Example.This is to be partially toward rolled surface from the base material near the rolling surface surface layer of titanium slab, and through-thickness stabilizes member to β phase
Plain concentration carries out the case where line analysis.It is found that β phase stabilizing element concentration is low in base material, become substantially uniform, but melting is coagulated again
Gu β phase stabilizes concentration height in layer, the vibration of concentration is further generated, there are inhomogeneities.
It as β phase stabilizing element, can enumerate: V, Mo, Fe, Cr, Mn, Ta, Nb, Ni, Co, Cu, W etc..However, fusing point
The elements such as high W, Ta become the reason of HDI (high density inclusions) in titanium, and holding does not melt, to spread insufficient state residual
The starting point of fatigue can be become when staying in titanium, therefore needed to pay attention to when use.In addition, Mo, Nb etc. be compared with W, Ta, fusing point
It is low, but fusing point is 2000 DEG C or more, therefore when use Mo, Nb, it is generally desirable to, the alloy with elements such as Ti is made in advance, makees
For the alloy addition for reducing fusing point.β phase stabilizing element can be divided into V, Mo, Ta, Nb etc. completely solid-solution type and Fe, Cr, Mn,
The eutectoid types such as Co, Ni, Cu, in eutectoid type, the solid solubility of each β phase stabilizing element is small, but to stabilize ability big for β phase, therefore altogether
The β phase stabilizing element of analysis type is also effective with a small amount of addition.In Fe, Cr, Mn, Co, Ni, Cu of eutectoid type, relative to
Base material can inhibit heat if the β phase stabilizing element concentration for melting again solidification layer is higher by 0.10~0.60 mass % or so
Surface blemish after rolling, therefore preferred above range.In V, Mo, Ta, Nb of complete solid-solution type, β phase stabilizes ability and analyses together
Type is compared to small, thus, it is desirable that relative to base material, 0.60 is had more to melt again the β phase stabilizing element concentration of solidification layer~
Largely add β phase stabilizing element in 1.50 mass % or so ground.In addition, even if using eutectoid type β phase stabilizing element, then melt
It being also quenched when solidification after melting, therefore cooling velocity is fast, does not generate precipitate, hot rolling also becomes two phase regions of alpha+beta when heating,
Therefore precipitate is not generated.In turn, it in the raw material containing β phase stabilizing element, also may include steady using Al as the α phase of representative
Surely change the neutral elements such as element, Sn, Zr.Also any one of α phase stabilizing element and neutral element or both be may include.
It is further preferred, that the total amount of α phase stabilizing element and neutral element in melting again solidification layer is set as relative to base material
2.0 mass % or less.It is preferable to use belong to β phase for the raw material melted together with the surface layer of the slab of state when maintaining casting
Stabilizing element and more cheap Fe, Ni, Cr.Using Fe powder etc., powder of stainless steel etc. or with crushing ordinary steel, no
The material obtained from the waste material of steel that becomes rusty is also effective.It is equally possible that using material obtained from the waste material for crushing titanium alloy
Material.
The raw material used for adding aforementioned β phase stabilizing element in the surface layer of slab can for powder, fragment,
Arbitrary shape in line, foil, desirably forms small pieces.Effectively, powder uses the raw material of the range of 1 μm~0.5mm of partial size,
Fragment uses the raw material of size 2mm square~5mm square range, and line uses the former material of the range of φ 0.5mm~φ 5mm
Material, foil use the raw material of the range of 1 μm~0.1mm of film thickness.When these raw material are placed or intersperse among the surface of slab, lead to
The surface for being equably configured at slab is crossed, can also equably be added to the surface layer of titanium slab, available surface texture is better
Good titanium slab.
In addition, thering is electron beam heating, electric arc heated, laser to add the method that surface layer melts together with β phase stabilizing element
The methods of heat and induction heating, but titanium is active metal, and when in an atmosphere melting surface layer, fusing department is obviously aoxidized, therefore
Suitable, the electron beam that can be handled in vacuum atmosphere or non-active gas atmosphere heats, electric arc heated is (special
Be plasma arc heating, TIG (Tungsten Inert Gas) welding etc. using inert gas heating means), laser
Heating etc., any means can carry out aforementioned processing.Wherein, it can disposably assign the electron beam heating of high-energy or wait
Gas ions electric arc heated be industrially it is suitable, be advisable using these methods.
Embodiment
Hereinafter, being further described in detail according to embodiment to the present invention.
[table 1]
In reference example shown in table 1, embodiment and comparative example, titanium slab is using electron-beam smelting, using each kind titanium
Alloy properties rectangular casting mould or cylinder mold and manufacture.Ingot casting by rectangular casting mould manufacture is thickness 200mm × wide
1000mm × length 4500mm is spent, is diameter by the ingot casting that cylinder mold manufactures using the hot rolled plate of hot rolling manufacture thickness 4mm
170mm × length 12m utilizes the wire rod of hot rolling manufacture diameter 13mm.It should be noted that hot rolling is the heat using steel material
What rolling plant carried out.As the raw material containing β phase stabilizing element, using powder (100 μm of partial size or less), (2mm is shown in fragment
Side, 1mm are thick), line (φ 1mm), any one of foil (20 μm).Titanium slab, which is fabricated to, not to carry out cutting finishing and is cut
Modify this 2 kinds, be rolling surface when containing β phase stabilizing element, keep cast(ing) surface state face (no cast(ing) surface
Cutting finishing) or machining face the cutting of cast(ing) surface (have modify) on directly place or spread and stabilized containing β phase
The raw material of element.Heating part is swept using electron beam and plasma arc from the heating for implementing slab surface layer thereon
It retouches, so that the whole face to rolling surface is handled, so that the non-fusing department of raw material and rolling surface comprising β phase stabilizing element
Do not remain.In addition, the titanium slab of state when maintaining casting uses the more good material of cast(ing) surface, so that molten on surface layer
Melting residual caused by not generated by cast(ing) surface when melting.In addition, in order to make β phase stabilizing element equably be added to slab
Whole, the rolling surface for making the raw material containing β phase stabilizing element be homogeneously dispersed in titanium slab is whole.Melt again solidification layer
The measuring method of depth is as follows: a part of the titanium slab solidified after surface layer being kept remelted is cut out, production embedment sample, and is ground
Mill, is supplied to SEM (Scaning Electron Microscopy)/EPMA (Electron Probe for gained sample
MicroAnalyser), carry out element mapping, so as to find out the embedment sample melting solidify again portion most superficial part depth, general
The depth is as the depth for melting again solidification layer.In addition, at this point, surface layer 1mm from any the 10 of the rolling surface of titanium slab with
Interior collection analysis sample carries out ICP and emits spectrophotometric analysis, takes the average value at 10.In addition, as a comparison, being cast by titanium
Before the surface layer of base is remelted, from any the 3 of the rolling surface of titanium slab from surface layer 20mm within collection analysis sample, similarly into
Row ICP emits spectrophotometric analysis, takes the average value at 3.For 2 kinds of the analysis as a result, investigation is until melt solidification layer again
In depth 1mm until in the range of β phase stabilizing element concentration average value and the β phase stabilizing element in base material
Difference between the average value of concentration.In addition, for the production of surface blemish, after hot rolling, to hot rolled plate carry out shot-peening and
After pickling, the surface of titanium (hot rolled plate) is visually observed, and is evaluated.It should be noted that in pickling, by every 1
The single side of secondary rolling surface is molten to cut about 50 μm or so (in terms of two sides about 100 μm), after carrying out 1~2 pickling to plate, evaluates hot rolling
The surface texture of plate.It should be noted that being not carried out in the comparative example of the melt process on surface layer, the acquisition point within the 1mm of surface layer
Sample is analysed, is melted again in comparative example of the thickness lower than 1mm of solidification layer, the collection analysis sample out of melting again solidification layer.
No.1 to No.31 is the example using plate as object.
For the reference example, comparative example and embodiment of No.1 to No.5, the cutting of cast(ing) surface is carried out after ingot casting casting
Finishing removes cast(ing) surface.On the other hand, for the embodiment of No.6 to No.31, without cast(ing) surface after ingot casting casting
Cutting finishing.
For the reference example, comparative example, embodiment of No.1 to No.21, the ingot casting of Ti-1Fe-0.35O is used.
The reference example of No.1 is the case where passing through breaking down in the same manner as previous manufacturing method and manufacture.Due to implementing just
The surface blemish for rolling, therefore generating on the hot rolled plate after pickling is slight.
The comparative example of No.2 is the case where not implementing breaking down after the cutting of ingot casting is modified and manufacture.Due to not implementing breaking down,
Therefore coarse flaw is generated on the hot rolled plate after pickling.
The comparative example of No.3 be ingot casting cutting finishing after, do not add β phase stabilizing element and using electron beam heat into
The case where row melting solidifies processing again.The depth for melting again solidification layer is 1mm or more, and the surface blemish after hot rolling and pickling is basic
On be slight, but part also generates slightly coarse flaw.
The comparative example of No.4 is after the cutting of ingot casting is modified, uses Fe powder as β phase stabilizing element, utilizes electron beam
Heating is melted the case where solidifying processing again.The depth for melting again solidification layer is lower than 1mm, the surface blemish after hot rolling and pickling
Locally generating slightly coarse flaw.
The embodiment of No.5 is after the cutting of ingot casting is modified, uses Fe powder as β phase stabilizing element, utilizes electron beam
Heating is melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and melts solidification layer and base material again
The concentration difference of β phase stabilizing element be also 0.08 mass % or more and 1.50 mass % hereinafter, surface after hot rolling and pickling
Flaw is slight.
The embodiment of No.6 be without ingot casting cutting finishing, use Fe powder as β phase stabilizing element, utilize electricity
Beamlet heating is melted the case where solidifying processing again.Melting again solidification layer depth be 1mm or more, and melt again solidification layer with
The concentration difference of the β phase stabilizing element of base material is also 0.08 mass % or more and 1.50 mass % hereinafter, after hot rolling and pickling
Surface blemish is slight.
The embodiment of No.7 be without ingot casting cutting finishing, use Fe powder as β phase stabilizing element, utilize
Gas ions electric arc heated is melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and melting is coagulated again
Gu the concentration difference of layer and the β phase stabilizing element of base material is also 0.08 mass % or more and 1.50 mass % hereinafter, hot rolling and acid
Surface blemish after washing is slight.
The embodiment of No.8 to No.10 is made without the cutting finishing of ingot casting, respectively using Fe fragment, Fe line, Fe foil
The case where solidifying processing again is melted for β phase stabilizing element, using electron beam heating.The depth of melting solidification layer again is
1mm or more, and solidification layer and the concentration difference of the β phase stabilizing element of base material are also 0.08 mass % or more and 1.50 matter again for melting
% is measured hereinafter, the surface blemish after hot rolling and pickling is slight.
The embodiment of No.11 to No.17 is the cutting finishing without ingot casting, and it is steady to change β phase as β phase stabilizing element
Surely the type for changing element is Cr fragment, Ni fragment, Ti-Mo fragment, V fragment, Mn fragment, Co fragment, Cu fragment, utilizes electron beam
Heating is melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and melts solidification layer again and mother
The concentration difference of the β phase stabilizing element of material is also 0.08 mass % or more and 1.50 mass % hereinafter, table after hot rolling and pickling
Face flaw is slight.
The embodiment of No.18 to No.21 is the cutting finishing without ingot casting, as β phase stabilizing element, is used respectively
Fe-Nb fragment, SUS304 powder crush fragment (6-4V fragment) obtained from Ti-6 mass %Al-4 mass %V waste material, crush
Fragment (15-3-3-3 fragment) contains obtained from Ti-15 mass %V-3 mass %Cr-3 mass %Sn-3 mass %Al waste material
There are many materials of β phase stabilizing element and α phase stabilizing element, and the feelings for solidifying processing again are melted using electron beam heating
Condition.The depth for melting again solidification layer is 1mm or more, and melts again the concentration difference of solidification layer and the β phase stabilizing element of base material
Also for 0.08 mass % or more and 1.50 mass % are hereinafter, the surface blemish after hot rolling and pickling is slight.
The case where embodiment of No.22 to No.31 is the type of change titan alloy casting ingot, respectively, No.22 Ti-
The titanium alloy of 0.06 mass %Pd, No.23 are the titanium alloy of Ti-0.5 mass %Ni-0.05 mass %Ru, and No.24 is Ti-5 matter
The titanium alloy of %Al-1 mass %Fe is measured, No.25 is the titanium alloy of Ti-5 mass %Al-1 mass %Fe-0.25 mass %Si,
No.26 is the titanium alloy of Ti-3 mass %Al-2.5 mass %V, and No.27 is the titanium alloy of Ti-0.5 mass %Cu, and No.28 is
The titanium alloy of Ti-1 mass %Cu, No.29 are the titanium alloy of Ti-1 mass %Cu-0.5 mass %Nb, and No.30 is Ti-1 matter
The case where measuring %Cu-1 mass %Sn-0.3 mass %Si-0.2 mass %Nb, No.31 are Ti-3 mass %Al-5 mass %V's
Situation.It modifies without the cutting of ingot casting, is melted using Fe powder using electron beam heating as β phase stabilizing element
Melt the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and solidification layer and the β phase of base material are steady again for melting
Surely the concentration difference for changing element is also 0.08 mass % or more and 1.50 mass % hereinafter, the surface blemish after hot rolling and pickling is light
Micro-.
No.32 to No.41 is the example using wire rod as object.
For the reference example, comparative example and embodiment of No.32 to No.36, cutting for cast(ing) surface is carried out after ingot casting casting
Finishing is cut, cast(ing) surface is removed.On the other hand, for the embodiment of No.37 to No.41, without casting after ingot casting casting
The cutting on surface is modified.
For the reference example, comparative example, embodiment of No.32 to No.41, use Ti-3 mass %Al-2.5 mass %V's
Ingot casting.
The reference example of No.32 is the case where passing through breaking down in the same manner as previous manufacturing method and manufacture.Due to implementing just
The surface blemish for rolling, therefore generating on the hot rolled plate after pickling is slight.
The comparative example of No.33 is after the cutting of ingot casting is modified, the case where not implementing breaking down and manufacture.Due to not implementing just
It rolls, therefore generates coarse flaw on the hot rolled plate after pickling.
The comparative example of No.34 is not add β phase stabilizing element after the cutting finishing of ingot casting and electron beam is utilized to heat
Melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, the surface blemish base after hot rolling and pickling
It is slight in sheet, but part also generates slightly coarse flaw.
The comparative example of No.35 is after the cutting of ingot casting is modified, to use Fe foil as β phase stabilizing element, utilize electron beam
Heating is melted the case where solidifying processing again.The depth for melting again solidification layer is lower than 1mm, the surface blemish after hot rolling and pickling
Locally generating slightly coarse flaw.
The embodiment of No.36 is after the cutting of ingot casting is modified, to use Fe foil as β phase stabilizing element, utilize electron beam
Heating is melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and melts solidification layer and base material again
The concentration difference of β phase stabilizing element be also 0.08 mass % or more and 1.50 mass % hereinafter, surface after hot rolling and pickling
Flaw is slight.
The embodiment of No.37 is the cutting finishing without ingot casting, uses Fe foil as β phase stabilizing element, utilizes electricity
Beamlet heating is melted the case where solidifying processing again.Melting again solidification layer depth be 1mm or more, and melt again solidification layer with
The concentration difference of the β phase stabilizing element of base material is also 0.08 mass % or more and 1.50 mass % hereinafter, after hot rolling and pickling
Surface blemish is slight.
The embodiment of No.38 is the cutting finishing without ingot casting, uses Fe foil as β phase stabilizing element, utilizes
Gas ions electric arc heated is melted the case where solidifying processing again.The depth for melting again solidification layer is 1mm or more, and melting is coagulated again
Gu the concentration difference of layer and the β phase stabilizing element of base material is also 0.08 mass % or more and 1.50 mass % hereinafter, hot rolling and acid
Surface blemish after washing is slight.
The embodiment of No.39 and No.40 is the cutting finishing without ingot casting, as β phase stabilizing element, change β phase
The type of stabilizing element is Cr fragment, Ni fragment, is melted the case where solidifying processing again using electron beam heating.Melting is again
The depth of solidification layer is 1mm or more, and solidification layer and the concentration difference of the β phase stabilizing element of base material are also 0.08 matter again for melting
% or more and 1.50 mass % are measured hereinafter, the surface blemish after hot rolling and pickling is slight.
The embodiment of No.41 is modified without the cutting of ingot casting, as β phase stabilizing element, using including multiple β phases
The SUS304 powder of stabilizing element is melted the case where solidifying processing again using electron beam heating.Melt again solidification layer
Depth is 1mm or more, and solidification layer and the concentration difference of the β phase stabilizing element of base material are also 0.08 mass % or more again for melting
And 1.50 mass % hereinafter, the surface blemish after hot rolling and pickling is slight.
Claims (6)
1. a kind of hot rolling titanium slab, which is characterized in that it is the titanium slab comprising titanium alloy,
Having melting at the surface for becoming rolling surface, in the range more than depth 1mm, solidification layer, the melting solidify again again
Layer is the surface as rolling surface for making the titanium slab comprising titanium alloy and the β phase stabilizing element containing one or two or more kinds
Raw material melt together after, make its solidify obtained from,
The average value of the concentration of β phase stabilizing element in the range of until depth 1mm is in terms of quality % than the β phase in base material
The concentration of stabilizing element is higher by 0.08 mass % or more and 1.50 mass % or less.
2. hot rolling according to claim 1 titanium slab, wherein the β phase stabilizing element is one in Fe, Ni, Cr
Kind or two kinds or more.
3. hot rolling according to claim 1 titanium slab, wherein while containing the β phase stabilizing element, also contain
There are one or two or more kinds of α phase stabilizing element or neutral element.
4. a kind of hot rolling manufacturing method of titanium slab, wherein make the surface as rolling surface of the titanium slab comprising titanium alloy
After melting together with the raw material containing β phase stabilizing element, make its solidification, the β phase in the range of making until depth 1mm is steady
Surely change the concentration of element concentration of the average value in terms of quality % than the β phase stabilizing element in base material be higher by 0.08 mass % with
Upper and 1.50 mass % or less.
5. the hot rolling according to claim 4 manufacturing method of titanium slab, wherein described containing β phase stabilizing element
Raw material are powder, fragment, line, any form in foil.
6. the hot rolling according to claim 4 manufacturing method of titanium slab, wherein utilize electron beam heating or plasma
Heating makes the melt surface as rolling surface of the titanium slab comprising titanium alloy.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/JP2014/076083 WO2016051502A1 (en) | 2014-09-30 | 2014-09-30 | Titanium slab for hot rolling, and production method therefor |
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| CN107075688A CN107075688A (en) | 2017-08-18 |
| CN107075688B true CN107075688B (en) | 2019-06-18 |
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| US (1) | US20170349973A1 (en) |
| EP (1) | EP3202953A4 (en) |
| JP (1) | JP6075385B2 (en) |
| KR (1) | KR20170047339A (en) |
| CN (1) | CN107075688B (en) |
| EA (1) | EA201790491A1 (en) |
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| EA034378B1 (en) * | 2014-09-30 | 2020-01-31 | Ниппон Стил Корпорейшн | Titanium cast product for hot rolling and method for producing the same |
| CN115502202B (en) * | 2022-10-11 | 2024-05-24 | 攀钢集团攀枝花钢铁研究院有限公司 | Titanium and titanium alloy square billet processing method |
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|---|---|---|---|---|
| JPH09314278A (en) * | 1996-05-30 | 1997-12-09 | Fukushima Seiko Kk | Mold material for casting titanium and titanium alloy |
| JP2007332420A (en) * | 2006-06-15 | 2007-12-27 | Nippon Steel Corp | Method for producing titanium material and stock for hot rolling |
| CN105102679A (en) * | 2013-04-01 | 2015-11-25 | 新日铁住金株式会社 | Titanium slab for hot rolling and method for manufacturing same |
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|---|---|---|---|---|
| JPS6256561A (en) * | 1985-09-06 | 1987-03-12 | Honda Motor Co Ltd | Method for hardening surface of ti or ti alloy |
| JPH0776431B2 (en) * | 1987-12-11 | 1995-08-16 | 住友金属工業株式会社 | Surface hardening method for titanium products |
| JPH05148598A (en) * | 1991-02-20 | 1993-06-15 | Mitsubishi Materials Corp | Surface hardening method for base material consisting of titanium or titanium alloy and surface hardening member |
| JPH04272147A (en) * | 1991-02-25 | 1992-09-28 | Sumitomo Metal Ind Ltd | Production of titanium |
| JP2004115906A (en) * | 2002-09-20 | 2004-04-15 | Ichiro Kawakatsu | METHOD FOR COATING Al-Si ALLOY ON SUBSTRATE OF Ti OR Ti ALLOY |
| JP2007084855A (en) * | 2005-09-20 | 2007-04-05 | Yamaha Motor Co Ltd | Titanium member having black surface and manufacturing method therefor |
| KR101492356B1 (en) * | 2011-02-10 | 2015-02-10 | 신닛테츠스미킨 카부시키카이샤 | Abrasion-resistant titanium alloy member having excellent fatigue strength |
| JP2016128171A (en) * | 2013-04-01 | 2016-07-14 | 新日鐵住金株式会社 | Titanium hot rolling slab being hard to cause surface flaw and its manufacturing method |
| JP2014233753A (en) * | 2013-06-05 | 2014-12-15 | 新日鐵住金株式会社 | Industrial pure titanium ingot excellent in surface properties after hot rolling even if blooming process or fine arrangement process is omitted and method for manufacturing the same |
-
2014
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- 2014-09-30 UA UAA201702911A patent/UA116510C2/en unknown
- 2014-09-30 WO PCT/JP2014/076083 patent/WO2016051502A1/en active Application Filing
- 2014-09-30 JP JP2014549247A patent/JP6075385B2/en active Active
- 2014-09-30 EP EP14903243.5A patent/EP3202953A4/en not_active Withdrawn
- 2014-09-30 KR KR1020177008318A patent/KR20170047339A/en not_active Application Discontinuation
- 2014-09-30 CN CN201480082171.1A patent/CN107075688B/en active Active
- 2014-09-30 US US15/513,776 patent/US20170349973A1/en not_active Abandoned
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH09314278A (en) * | 1996-05-30 | 1997-12-09 | Fukushima Seiko Kk | Mold material for casting titanium and titanium alloy |
| JP2007332420A (en) * | 2006-06-15 | 2007-12-27 | Nippon Steel Corp | Method for producing titanium material and stock for hot rolling |
| CN105102679A (en) * | 2013-04-01 | 2015-11-25 | 新日铁住金株式会社 | Titanium slab for hot rolling and method for manufacturing same |
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| WO2016051502A1 (en) | 2016-04-07 |
| EP3202953A4 (en) | 2018-05-09 |
| US20170349973A1 (en) | 2017-12-07 |
| CN107075688A (en) | 2017-08-18 |
| EP3202953A1 (en) | 2017-08-09 |
| JPWO2016051502A1 (en) | 2017-04-27 |
| EA201790491A1 (en) | 2017-07-31 |
| UA116510C2 (en) | 2018-03-26 |
| KR20170047339A (en) | 2017-05-04 |
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