WO2016051502A1 - 熱間圧延用チタン鋳片およびその製造方法 - Google Patents
熱間圧延用チタン鋳片およびその製造方法 Download PDFInfo
- Publication number
- WO2016051502A1 WO2016051502A1 PCT/JP2014/076083 JP2014076083W WO2016051502A1 WO 2016051502 A1 WO2016051502 A1 WO 2016051502A1 JP 2014076083 W JP2014076083 W JP 2014076083W WO 2016051502 A1 WO2016051502 A1 WO 2016051502A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- stabilizing element
- titanium
- phase stabilizing
- mass
- hot rolling
- Prior art date
Links
- 239000010936 titanium Substances 0.000 title claims abstract description 86
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 84
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 83
- 238000005098 hot rolling Methods 0.000 title claims description 47
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- 238000010438 heat treatment Methods 0.000 claims abstract description 40
- 238000010894 electron beam technology Methods 0.000 claims abstract description 31
- 229910001069 Ti alloy Inorganic materials 0.000 claims abstract description 19
- 239000000843 powder Substances 0.000 claims abstract description 16
- 239000011888 foil Substances 0.000 claims abstract description 11
- 230000000087 stabilizing effect Effects 0.000 claims description 112
- 239000000463 material Substances 0.000 claims description 68
- 238000005096 rolling process Methods 0.000 claims description 17
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 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 68
- 238000000034 method Methods 0.000 abstract description 57
- 239000002344 surface layer Substances 0.000 abstract description 40
- 230000008018 melting Effects 0.000 abstract description 35
- 238000002844 melting Methods 0.000 abstract description 35
- 239000002994 raw material Substances 0.000 abstract description 5
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- 239000000155 melt Substances 0.000 description 50
- 230000008569 process Effects 0.000 description 30
- 238000005554 pickling Methods 0.000 description 23
- 230000037303 wrinkles Effects 0.000 description 22
- 238000005266 casting Methods 0.000 description 15
- 239000013078 crystal Substances 0.000 description 14
- 230000015556 catabolic process Effects 0.000 description 13
- 230000000052 comparative effect Effects 0.000 description 13
- 238000005520 cutting process Methods 0.000 description 12
- 230000007547 defect Effects 0.000 description 12
- 239000000523 sample Substances 0.000 description 9
- 238000007711 solidification Methods 0.000 description 9
- 230000009466 transformation Effects 0.000 description 8
- 239000011324 bead Substances 0.000 description 7
- 229910052758 niobium Inorganic materials 0.000 description 7
- 229910052720 vanadium Inorganic materials 0.000 description 7
- 238000004458 analytical method Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 229910052802 copper Inorganic materials 0.000 description 5
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- 230000008023 solidification Effects 0.000 description 5
- 229910052715 tantalum Inorganic materials 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000005422 blasting Methods 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 230000009467 reduction Effects 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
- 239000011261 inert gas Substances 0.000 description 3
- 238000004093 laser heating Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000004611 spectroscopical analysis Methods 0.000 description 2
- 230000006641 stabilisation Effects 0.000 description 2
- 238000011105 stabilization Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 239000004484 Briquette Substances 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 229910011214 Ti—Mo Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000010891 electric arc Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 238000013507 mapping Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation 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
- 238000005498 polishing Methods 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 229910052707 ruthenium Inorganic materials 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 150000003608 titanium Chemical class 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
Images
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
Definitions
- the present invention is a method for producing a titanium slab for hot rolling made of a titanium alloy, and in particular, even if a breakdown process such as block rolling or forging is omitted, the surface properties after hot rolling are excellent.
- the present invention relates to a titanium slab that can be maintained and a method for manufacturing the same.
- the titanium material is generally made of sponge titanium or titanium scrap as a raw material, and is melted by a non-consumable electrode type arc melting method, an electron beam melting method, a plasma arc melting method or the like to form a titanium ingot (titanium cast).
- a non-consumable electrode type arc melting method an ingot is obtained by using a briquette formed by pressurizing sponge titanium as an electrode, causing arc discharge between the electrode and the mold, melting the electrode itself, and casting in the mold. Therefore, since it is necessary to discharge the mold and the electrode uniformly, the mold shape is limited to a cylindrical shape, and the ingot shape after casting is a columnar shape.
- the electron beam melting method and the plasma arc melting method use an electron beam and a plasma arc, respectively.
- the melting method is different, but the molten titanium melted on the hearth is poured into the mold at the time of melting. It is possible to manufacture ingots having various shapes such as a rectangular shape and a billet shape.
- the ingot breakdown process In the current titanium material manufacturing process, after the hot working process such as ingot rolling and forging, which is called the ingot breakdown process, hot rolling is performed, and a breakdown process is required. ing. However, because of its shape, it is considered that the breakdown process can be omitted at the time of manufacturing a plate material for rectangular ingots (slab-shaped ingots), and at the time of manufacturing rods and wires for cylindrical and billet-shaped ingots. Techniques for omitting hot rolling have been studied. Once this technology is established, cost reductions can be expected by omitting the process and improving yield.
- titanium slabs manufactured by using the electron beam melting method or the plasma arc melting method are as cast, and therefore there are coarse grains of several tens of millimeters.
- Such a titanium cast slab is subjected to hot rolling while omitting the breakdown step, irregularities are produced on the surface due to the influence of deformation anisotropy within the grains and between each crystal grain due to coarse grains. This becomes a surface defect.
- titanium ingots manufactured by the electron beam melting method or the plasma arc melting method are expected to improve costs by omitting breakdown processes such as ingot rolling and forging, but there is a concern about an increase in costs due to an increase in surface defects. This has hindered the practical application of titanium slabs without the breakdown process.
- Patent Document 1 in a cross-sectional structure of a titanium slab melted in an electron beam melting furnace and directly pulled out from the mold, an angle ⁇ formed by a solidification direction from the surface layer to the inside and a casting direction of the slab is 45 ° to 90 °, Or, in the crystal orientation distribution of the surface layer, when the angle between the hcp c-axis and the normal of the slab surface layer is 35 ° to 90 °, the casting surface is good and the breakdown process of the ingot is omitted.
- a method is disclosed that can improve the surface defects after hot rolling. That is, the generation of wrinkles due to such coarse crystal grains can be suppressed by controlling the shape and crystal orientation of the surface crystal grains.
- Patent Document 2 as a method of directly performing hot rolling while omitting the breakdown process of the titanium material ingot, the surface layer corresponding to the rolling surface is subjected to high frequency induction heating, arc heating, plasma heating, electron beam heating, laser heating, etc. By remelting and re-solidifying, a fine particle having a depth of 1 mm or more is performed from the surface layer. Generation of surface defects is prevented by providing a fine and irregular crystal orientation distribution by rapid solidification of the slab surface layer.
- the present invention not only omits the breakdown process but also eliminates the need for a cutting and refining process of the titanium cast slab surface layer as cast, and suppresses the occurrence of surface flaws in the titanium material after subsequent hot rolling and A manufacturing method thereof is provided.
- the present invention is as follows.
- a titanium slab made of a titanium alloy One or two or more kinds of ⁇ -phase stabilizing elements are added to the surface to be the rolled surface, and the molten and resolidified layer is melted and resolidified in a depth range of 1 mm or more.
- the average value of the concentration of the ⁇ -phase stabilizing element in the range up to a depth of 1 mm is 0.08 mass% or more and 1.50 mass% or less in mass% compared to the concentration of the ⁇ -phase stabilizing element in the base material.
- a titanium cast for hot rolling characterized by being high.
- the titanium slab for hot rolling according to (1) which contains one or more ⁇ -phase stabilizing elements or neutral elements together with the ⁇ -phase stabilizing element.
- a method for producing a titanium slab for hot rolling in which a rolling surface of a titanium slab made of a titanium alloy is melted together with a material containing a ⁇ -phase stabilizing element and then solidified.
- the titanium slab of the present invention produces a titanium material having surface properties equivalent to those of the conventional material even when hot rolling is performed by omitting the breakdown steps such as ingot rolling and forging that were conventionally necessary. Is possible. Reduction of heating time by omitting the breakdown process, reduction of cutting care due to smoothing of the surface layer of the titanium slab by surface melting, reduction of the amount of cutting during pickling by improving the surface properties of the titanium material after hot rolling Thus, since the yield is improved, the production cost can be reduced, and the industrial effect is immeasurable.
- a titanium alloy is manufactured into a shape such as a plate, a wire, or a bar by performing hot rolling or cold rolling.
- the titanium alloy refers to an ⁇ -type titanium alloy and an ⁇ + ⁇ -type titanium alloy.
- the titanium slabs targeted by the present invention are rectangular ingots (slab-shaped ingots), columnar ingots, and billet-shaped ingots. This is a technique for suppressing surface flaws on a titanium material after hot rolling by melting the surface layer of a titanium cast slab of these shapes together with a material containing a ⁇ -phase stabilizing element.
- melt re-solidified layer When cooled to room temperature (in this way, only the surface part of the as-cast titanium slab is melted by heating,
- the cross-sectional structure of the solidified layer that has been rapidly cooled and then solidified again is referred to as a “melt re-solidified layer”) becomes a fine acicular structure or a martensitic structure.
- the melt re-solidified layer can be made to have a finer structure by causing the ⁇ phase transformation or the martensite transformation during cooling.
- “Hardenability improvement” here refers to the inclusion of a ⁇ -phase stabilizing element in the surface layer of the titanium slab, and by shifting the nose of the transformation during continuous cooling to a longer time side, the ⁇ -phase transformation at a low temperature. Refers to the transformation or martensitic transformation. The purpose is to increase the number of nucleation sites and to refine crystal grains by transformation at low temperature.
- the melt resolidification layer is in an ⁇ + ⁇ two-phase region during hot rolling heating, and ⁇
- the phase and the ⁇ phase grain growth is suppressed, and fine crystal grains after melt resolidification can be maintained as fine grains until hot rolling after hot rolling heating. Therefore, it was found that the unevenness of the surface of the titanium material due to the coarse crystal grains can be suppressed, and a titanium hot-rolled material that does not generate surface flaws can be produced.
- the formed melt-resolidified layer has a deep portion and a shallow portion.
- the depth of the molten resolidified layer is 1 mm or more, and this depth refers to the depth of the shallowest portion when viewed in a cross section perpendicular to the scanning direction of the molten bead.
- the surface layer of titanium cast slab with a depth of 1 mm or more as described above solidification results in a fine acicular structure or martensite structure with a depth of 1 mm or more from the surface layer.
- the center side in the thickness direction of the titanium material plate from the heat-affected zone is a cast structure.
- at least the surface layer corresponding to the rolling surface of the titanium slab is remelted together with the material containing the ⁇ -phase stabilizing element, and then solidified to stabilize the ⁇ -phase from the surface layer in the molten re-solidified layer to a depth of 1 mm.
- the average value of the concentration of the chemical element is characterized by a certain amount higher than the concentration of the ⁇ -phase stabilizing element in the base material.
- the ⁇ + ⁇ type titanium alloy containing the ⁇ phase stabilizing element as the alloy composition has the effect of refining the crystal grains of the melt resolidified layer.
- the composition of the melted part at the time of the melt resolidification process is such that when the surface layer is melted together with the ⁇ -phase stabilizing element, solidification starts immediately after melting, so that diffusion does not occur sufficiently in the melted part. Inhomogeneity of the phase stabilizing element concentration remains. When such non-uniformity remains, a region having a high ⁇ -phase stabilizing element concentration is generated, resulting in a finer structure.
- the average value of the concentration of the ⁇ -phase stabilizing element from the surface layer in the melt-resolidified layer to a depth of 1 mm is 0.08 mass% or more and 1.50 mass in mass% compared to the concentration of the ⁇ -phase stabilizing element in the base material. It is sufficient that the content is higher than%.
- the ⁇ -phase stabilizing element may be added in combination with a plurality of ⁇ -phase stabilizing elements. In this case, the concentration of the ⁇ -phase stabilizing element indicates the sum of the concentrations of the contained ⁇ -phase stabilizing elements.
- the concentration difference of the ⁇ -phase stabilizing element is preferably more than 0.2 mass%, and more preferably more than 0.5 mass%. Further, if the difference in concentration of the ⁇ -phase stabilizing element between the base material and the melt-resolidified layer is within the above range, the ⁇ -phase stabilizing element in the surface layer by the shot blasting and pickling processes, which is a process after hot rolling.
- the ⁇ -phase stabilizing element concentrated in the melted and resolidified layer is rendered harmless. That is, by performing the shot blasting and pickling steps, the ⁇ -phase stabilizing element concentrated layer is eliminated, and the components and mechanical properties are the same as those of a cold-rolled sheet manufactured by a normal manufacturing method. However, when the difference in concentration of the ⁇ -phase stabilizing element between the base material and the melt-resolidified layer is higher than 1.50 mass%, the ratio of the ⁇ phase that is markedly oxidized in the surface layer of the titanium slab increases.
- the amount of oxidation greatly increases, and further, the difference in hot deformation resistance between the molten resolidified layer and the base material of the surface of the titanium slab during hot rolling becomes large, and cracks and the like occur at the surface layer and the above-mentioned boundary portion. There is a case. From these factors, it is necessary to increase the amount of surface cutting in the pickling process, and the yield is significantly reduced. In addition, since it is difficult to render the concentrated layer of the ⁇ -phase stabilizing element harmless in the subsequent process, the average value of the concentration of the ⁇ -phase stabilizing element from the surface layer to a depth of 1 mm is the ⁇ -phase stabilization of the base material. The element concentration was set to 1.50 mass% or less.
- the melt depth is set to 1 mm or more, there is a concern that a concentrated layer of the ⁇ -phase stabilizing element may remain after the shot blasting and pickling steps if the melt depth becomes too deep.
- the length is desirably up to about 5 mm.
- the composition of the titanium slab slightly differs depending on the distribution of the solute for each element.
- ⁇ -phase stabilizing elements such as Fe are elements that show positive segregation, the Fe concentration in the surface layer portion of the titanium slab decreases during solidification and transformation, and the Fe concentration tends to increase toward the inside of the titanium slab. It is in. Therefore, it is extremely effective to make the ⁇ -phase stabilizing element concentration in the melted and re-solidified layer equal to or higher than the base material by melting the ⁇ -phase stabilizing element and the base material at the same time. This effect is particularly remarkable in the ⁇ -type titanium alloy.
- the amount of raw material is controlled to adjust the slab components uniformly.
- component variations may occur.
- Surface flaws may occur. Therefore, it is effective to base up the amount of ⁇ -phase stabilizing element added by adding a ⁇ -stabilizing element at the time of melting and re-solidification, and it is possible to suppress partial surface defects. .
- the component variation of the ⁇ -stabilizing element in the melt-solidified phase is larger than the component variation of the base material even in the originally high ⁇ -stabilizing element concentration, so the effect of dividing the colony is more It becomes large, and it becomes possible to suppress surface wrinkles that partially occur.
- the shape of the molten resolidified layer tends to be deepest at the center of the molten bead when the titanium slab surface layer is remelted, and when the molten beads are stacked, It becomes the shallowest in the middle between adjacent molten beads, and takes the form that the deepest part and the shallowest part are repeated periodically.
- the difference between the deepest part and the shallowest part is large, the difference in deformation resistance is caused by this difference during hot rolling, and wrinkles resulting from this may occur. Therefore, the difference is desirably less than 2 mm.
- the depth of the melt-resolidified layer is 1 mm or more, and this depth refers to the depth of the shallowest portion when viewed in a cross section perpendicular to the scanning direction of the molten bead. .
- FIG. 1 shows an example of measured values of the concentration change of the base material and the melted / solidified layer.
- a ⁇ -phase stabilizing element concentration is linearly analyzed in the thickness direction from the base material portion near the surface layer of the rolled surface of the titanium cast piece toward the rolling surface. It can be seen that the ⁇ -phase stabilizing element concentration is low and almost uniform in the base material, but the ⁇ -phase stabilizing concentration is high in the melted and re-solidified layer, and the concentration fluctuates, and there is non-uniformity.
- Examples of ⁇ -phase stabilizing elements include V, Mo, Fe, Cr, Mn, Ta, Nb, Ni, Co, Cu, and W.
- W and Ta which have a high melting point, cause HDI (high density inclusions), and if they remain in the titanium material without being melted or insufficiently diffused, they become the starting point of fatigue. Care must be taken to do this.
- Mo and Nb have lower melting points than W and Ta, but the melting point is 2000 ° C. or higher. Therefore, when using Mo or Nb, an alloy with a lower melting point as an alloy with an element such as Ti in advance is used. It is desirable to add.
- ⁇ -phase stabilizing elements can be classified into solid solution types such as V, Mo, Ta, and Nb, and eutectoid types such as Fe, Cr, Mn, Co, Ni, and Cu. Although the solid solubility of the ⁇ -phase stabilizing element is small, but the ⁇ -phase stabilizing ability is large, the eutectoid ⁇ -phase stabilizing element is effective even when added in a small amount.
- the surface after hot rolling if the ⁇ -phase stabilizing element concentration of the molten resolidified layer relative to the base material is as high as about 0.10 to 0.60 mass%. The above range is preferable because wrinkles can be suppressed.
- the ⁇ -phase stabilizing ability is smaller than that of the eutectoid type. It is desirable to add a large amount of ⁇ -phase stabilizing element to about ⁇ 1.50 mass%. Even if a eutectoid ⁇ -phase stabilizing element is used, since it is rapidly cooled during solidification after remelting, the cooling rate is fast, no precipitates are formed, and a two-phase region of ⁇ + ⁇ is also obtained during hot rolling heating. Therefore, no precipitate is generated. Furthermore, the material containing the ⁇ -phase stabilizing element may contain an ⁇ -phase stabilizing element typified by Al, or a neutral element such as Sn or Zr.
- Either one or both of the ⁇ -phase stabilizing element and the neutral element may be contained. Moreover, it is preferable that the total amount of the ⁇ -phase stabilizing element and the neutral element in the melt-resolidified layer with respect to the base material is 2.0 mass% or less. It is preferable to use Fe, Ni, and Cr, which are ⁇ -phase stabilizing elements and relatively inexpensive, as the material that melts together with the surface layer of the as-cast slab. It is also effective to use Fe powder, stainless steel powder, etc., or to use crushed plain steel or stainless steel scrap. Similarly, a crushed titanium alloy scrap may be used.
- the material used for adding the ⁇ -phase stabilizing element to the surface layer of the slab may be any shape of powder, chip, wire, and foil, and is preferably a small piece. It is effective to use a powder with a particle size of 1 ⁇ m to 0.5 mm, a chip with a size of 2 mm square to 5 mm square, a wire with ⁇ 0.5 mm to ⁇ 5 mm, and a foil with a thickness of 1 ⁇ m to 0.1 mm. It is. These materials can be evenly added to the surface of the titanium slab by placing it uniformly on the surface of the slab when it is placed or spread on the surface of the slab. The titanium cast slab is obtained.
- Electron beam heating and arc heating (especially heating methods using inert gas such as plasma arc heating or TIG (Tungsten Inert Gas) welding) that can be processed in a vacuum atmosphere or an inert gas atmosphere because the molten part is significantly oxidized, laser Heating or the like is suitable, and the above treatment can be performed by any method.
- electron beam heating or plasma arc heating capable of imparting high energy at a time is industrially suitable, and these methods are preferably used.
- the titanium cast slabs are manufactured by using electron beam melting and using various types of titanium alloy rectangular or cylindrical molds.
- the ingot manufactured from the rectangular mold is 200 mm thick ⁇ 1000 mm wide ⁇ 4500 mm long, hot rolled into a hot rolled sheet 4 mm thick, the ingot manufactured from the cylindrical mold is 170 mm in diameter ⁇ 12 m in length, A wire rod having a diameter of 13 mm was produced by hot rolling.
- the hot rolling was performed using a hot rolling facility for steel materials.
- Titanium cast slabs are manufactured in two types: those that do not undergo cutting care, and those that do include a ⁇ -phase stabilizing element, both of which are rolled surfaces, as-cast surfaces (cutting care for casting surfaces) None), or a material containing a ⁇ -phase stabilizing element was placed or sprayed on the cut surface (with the cut surface of the casting surface).
- the surface of the slab is heated from above, and the entire heated surface is processed by scanning the heated portion with an electron beam and a plasma arc.
- the material containing the ⁇ -phase stabilizing element and the unmelted portion of the rolled surface was not left.
- as-cast titanium slabs have a relatively good casting surface, so that no unmelted residue due to the casting surface occurs when the surface layer melts.
- the raw material containing a ⁇ phase stabilizing element was uniformly dispersed throughout the rolled surface of the titanium slab so that the ⁇ phase stabilizing element was uniformly added to the entire slab.
- the method of measuring the depth of the melted and resolidified layer is to cut a part of a cast titanium piece that has been solidified after remelting the surface layer, prepare an embedded sample, and polish the SEM (Scanning Electron Microscope) / EPMA (Electron Probe MicroAnalyzer).
- the depth of the shallowest part of the melted and resolidified portion of the embedded sample was determined, and the depth was taken as the depth of the melted and resolidified layer.
- an analysis sample was taken from within 1 mm of the surface layer of any 10 places on the rolled surface of the titanium cast slab, and subjected to ICP emission spectroscopic analysis to obtain an average value at 10 places. Further, as a comparison, before remelting the surface layer of the titanium slab, an analysis sample was taken from any three surface layers within 20 mm of the rolled surface of the titanium slab, and the ICP emission spectroscopic analysis was similarly performed. The average value was taken.
- the difference between the average value of the ⁇ -phase stabilizing element concentration in the range up to 1 mm in the melt-resolidified layer and the average value of the ⁇ -phase stabilizing element concentration in the base metal is investigated. Further, the occurrence of surface defects was evaluated by visually observing the surface of the titanium material (hot rolled plate) after hot rolling, shot blasting and pickling the hot rolled plate. In pickling, one side of the rolled surface is cut by about 50 ⁇ m (about 100 ⁇ m on both sides), and the surface properties of the hot-rolled sheet are evaluated after passing the pickling once or twice. .
- the analysis sample was collected from within 1 mm of the surface layer, and in the comparative example in which the thickness of the molten resolidified layer was less than 1 mm, the analysis sample was collected from within the molten resolidified layer. .
- Reference numeral 31 is an example for a plate material.
- a reference example 1 is a case of being manufactured through split rolling in the same manner as the conventional manufacturing method. Since surface rolling was performed, the surface defects generated on the hot-rolled sheet after pickling were slight.
- the comparative example 2 is a case where the ingot was manufactured without cutting after ingot cutting. Since the bulk rolling was not performed, coarse wrinkles were generated on the hot-rolled sheet after pickling.
- the comparative example 3 is a case where the melt resolidification treatment is performed by electron beam heating without adding the ⁇ -phase stabilizing element after the ingot is cut and cared for.
- the depth of the melt-resolidified layer was 1 mm or more, and the surface defects after hot rolling and pickling were basically slight, but partially coarse defects were also generated.
- the comparative example 4 is a case where, after cutting the ingot, Fe powder is used as the ⁇ -phase stabilizing element, and melt resolidification treatment is performed by electron beam heating.
- the depth of the melt-resolidified layer was less than 1 mm, and the surface wrinkles after hot rolling and pickling partially generated slightly coarse wrinkles.
- Example 5 is a case in which after the ingot is cut and carved, Fe powder is used as a ⁇ -phase stabilizing element, and melt resolidification treatment is performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- Example 6 the ingot was not cut and carved, and Fe powder was used as the ⁇ -phase stabilizing element, and the melt resolidification process was performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- Example 7 is a case where the ingot is not cut and maintained, Fe powder is used as the ⁇ -phase stabilizing element, and the melt resolidification process is performed by plasma arc heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- the ingot is not cut and maintained, and the Fe-phase, Fe wire, and Fe foil are used as ⁇ -phase stabilizing elements, respectively, and the melt resolidification process is performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the difference in concentration of the ⁇ -phase stabilizing element between the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. The surface wrinkle after pickling was slight.
- the ingot is not cut and maintained, and the Cr phase, Ni chip, Ti—Mo chip, V chip, Mn chip, Co chip, Cu chip and ⁇ phase stabilizing element are used as the ⁇ phase stabilizing element.
- the melt re-solidification process is performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the difference in concentration of the ⁇ -phase stabilizing element between the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less.
- the surface wrinkle after pickling was slight.
- Example 21 the ingot was not cut and maintained, and Fe-Nb chips, SUS304 powder, Ti-6 mass% Al-4 mass% V scrap ground chips (6-4V chips), Ti -15 mass% V-3 mass% Cr-3 mass% Sn-3 mass% Al scrap scraped chip (15-3-3-3 chip) ⁇ -phase stabilizing element and material containing several kinds of ⁇ -phase stabilizing element
- the melt resolidification process is performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more
- the difference in concentration of the ⁇ -phase stabilizing element between the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less.
- the surface wrinkle after pickling was slight.
- No. 22 to No. The example of 31 is a case where the kind of titanium alloy ingot is changed.
- No. 22 is Ti-0.06 mass% Pd
- No. 22 No. 23 is Ti-0.5 mass% Ni-0.05 mass% Ru
- No. 24 is Ti-5 mass% Al-1 mass% Fe
- No. 25 is Ti-5 mass% Al-1 mass% Fe-0.25 mass% Si
- No. 25 No. 26 is Ti-3 mass% Al-2.5 mass% V
- No. 26. 27 is Ti-0.5 mass% Cu
- No. 27. 28 is Ti-1 mass% Cu
- No. 28 No.
- No. 29 is a titanium alloy of Ti-1 mass% Cu-0.5 mass% Nb, No. 29. No.
- No. 32 to No. 41 is an example for a wire.
- a reference example of 32 is a case where it is manufactured through split rolling similarly to the conventional manufacturing method. Since surface rolling was performed, the surface defects generated on the hot-rolled sheet after pickling were slight.
- the comparative example of 33 is a case where it manufactured without implementing ingot rolling after the ingot cutting care. Since the bulk rolling was not performed, coarse wrinkles were generated on the hot-rolled sheet after pickling.
- the comparative example 34 is a case where after the ingot is cut and carved, the melt resolidification process is performed by electron beam heating without adding the ⁇ -phase stabilizing element.
- the depth of the melt-resolidified layer was 1 mm or more, and the surface defects after hot rolling and pickling were basically slight, but partially coarse defects were also generated.
- the comparative example No. 35 is a case where after the ingot is cut and carved, an Fe foil is used as the ⁇ -phase stabilizing element and the melt resolidification process is performed by electron beam heating.
- the depth of the melt-resolidified layer was less than 1 mm, and the surface wrinkles after hot rolling and pickling partially generated slightly coarse wrinkles.
- the example of 36 is a case where after the ingot is cut and carved, Fe foil is used as the ⁇ -phase stabilizing element, and the melt resolidification process is performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- Example 37 the ingot was not cut and carved, and Fe foil was used as the ⁇ -phase stabilizing element, and melt resolidification treatment was performed by electron beam heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- the example of 38 is a case where the ingot is not cut and maintained, and Fe refining element is used as the ⁇ -phase stabilizing element and the melt resolidification process is performed by plasma arc heating.
- the depth of the melt resolidified layer is 1 mm or more, and the concentration difference between the ⁇ phase stabilizing element of the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less. Later surface wrinkles were minor.
- the ingot was not cut and maintained, and the re-solidification treatment was performed by electron beam heating by changing the type of Cr chip, Ni chip and ⁇ phase stabilizing element as the ⁇ phase stabilizing element. is there.
- the depth of the melt resolidified layer is 1 mm or more, and the difference in concentration of the ⁇ -phase stabilizing element between the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less.
- the surface wrinkle after pickling was slight.
- Example 41 the ingot was not cut and carved, and SUS304 powder containing a plurality of ⁇ -phase stabilizing elements was used as the ⁇ -phase stabilizing element, and melt resolidification treatment was performed by electron beam heating. is there.
- the depth of the melt resolidified layer is 1 mm or more
- the difference in concentration of the ⁇ -phase stabilizing element between the melt resolidified layer and the base material is 0.08 mass% or more and 1.50 mass% or less.
- the surface wrinkle after pickling was slight.
Landscapes
- 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)
- Manufacture And Refinement Of Metals (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Continuous Casting (AREA)
Abstract
Description
(1)
チタン合金からなるチタン鋳片であって、
圧延面となる表面に、一種または二種類以上のβ相安定化元素を添加して溶融させ再凝固させた溶融再凝固層を深さ1mm以上の範囲に有し、
深さ1mmまでの範囲におけるβ相安定化元素の濃度の平均値が、母材中のβ相安定化元素の濃度に比較して、質量%で、0.08mass%以上、1.50mass%以下高いことを特徴とする、熱間圧延用チタン鋳片。
(2)
前記β相安定化元素が、Fe、Ni、Crの一種または二種以上である、(1)に記載の熱間圧延用チタン鋳片。
(3)
前記β相安定化元素とともに、α相安定化元素もしくは中性元素を一種または二種以上含有する、(1)に記載の熱間圧延用チタン鋳片。
(4)
チタン合金からなるチタン鋳片の圧延面となる表面を、β相安定化元素を含有する素材とともに溶融させた後、凝固させる、熱間圧延用チタン鋳片の製造方法。
(5)
前記β相安定化元素を含有する素材が、粉末、チップ、ワイヤー、箔のいずれかの形態である、(4)に記載の熱間圧延用チタン鋳片の製造方法。
(6)
前記チタン合金からなるチタン鋳片の圧延面となる表面を、電子ビーム加熱またはプラズマ加熱によって溶融させる、(4)に記載の熱間圧延用チタン鋳片の製造方法。
Claims (6)
- チタン合金からなるチタン鋳片であって、
圧延面となる表面に、一種または二種類以上のβ相安定化元素を添加して溶融させ再凝固させた溶融再凝固層を深さ1mm以上の範囲に有し、
深さ1mmまでの範囲におけるβ相安定化元素の濃度の平均値が、母材中のβ相安定化元素の濃度に比較して、質量%で、0.08mass%以上、1.50mass%以下高いことを特徴とする、熱間圧延用チタン鋳片。 - 前記β相安定化元素が、Fe、Ni、Crの一種または二種以上である、請求項1に記載の熱間圧延用チタン鋳片。
- 前記β相安定化元素とともに、α相安定化元素もしくは中性元素を一種または二種以上含有する、請求項1に記載の熱間圧延用チタン鋳片。
- チタン合金からなるチタン鋳片の圧延面となる表面を、β相安定化元素を含有する素材とともに溶融させた後、凝固させる、熱間圧延用チタン鋳片の製造方法。
- 前記β相安定化元素を含有する素材が、粉末、チップ、ワイヤー、箔のいずれかの形態である、請求項4に記載の熱間圧延用チタン鋳片の製造方法。
- 前記チタン合金からなるチタン鋳片の圧延面となる表面を、電子ビーム加熱またはプラズマ加熱によって溶融させる、請求項4に記載の熱間圧延用チタン鋳片の製造方法。
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
UAA201702911A UA116510C2 (uk) | 2014-09-30 | 2014-09-30 | Титановий виливок для гарячої прокатки і спосіб його виготовлення |
PCT/JP2014/076083 WO2016051502A1 (ja) | 2014-09-30 | 2014-09-30 | 熱間圧延用チタン鋳片およびその製造方法 |
EA201790491A EA201790491A1 (ru) | 2014-09-30 | 2014-09-30 | Титановая отливка для горячей прокатки и способ ее изготовления |
EP14903243.5A EP3202953A4 (en) | 2014-09-30 | 2014-09-30 | Titanium slab for hot rolling, and production method therefor |
JP2014549247A JP6075385B2 (ja) | 2014-09-30 | 2014-09-30 | 熱間圧延用チタン鋳片およびその製造方法 |
CN201480082171.1A CN107075688B (zh) | 2014-09-30 | 2014-09-30 | 热轧用钛铸坯及其制造方法 |
US15/513,776 US20170349973A1 (en) | 2014-09-30 | 2014-09-30 | Titanium casting product for hot rolling and method for producing the same |
KR1020177008318A KR20170047339A (ko) | 2014-09-30 | 2014-09-30 | 열간 압연용 티타늄 주조편 및 그 제조 방법 |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP2014/076083 WO2016051502A1 (ja) | 2014-09-30 | 2014-09-30 | 熱間圧延用チタン鋳片およびその製造方法 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2016051502A1 true WO2016051502A1 (ja) | 2016-04-07 |
Family
ID=55629600
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2014/076083 WO2016051502A1 (ja) | 2014-09-30 | 2014-09-30 | 熱間圧延用チタン鋳片およびその製造方法 |
Country Status (8)
Country | Link |
---|---|
US (1) | US20170349973A1 (ja) |
EP (1) | EP3202953A4 (ja) |
JP (1) | JP6075385B2 (ja) |
KR (1) | KR20170047339A (ja) |
CN (1) | CN107075688B (ja) |
EA (1) | EA201790491A1 (ja) |
UA (1) | UA116510C2 (ja) |
WO (1) | WO2016051502A1 (ja) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
UA116511C2 (uk) * | 2014-09-30 | 2018-03-26 | Ніппон Стіл Енд Сумітомо Метал Корпорейшн | Виливок з титану для гарячої прокатки і спосіб його виробництва |
CN115502202B (zh) * | 2022-10-11 | 2024-05-24 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种钛及钛合金方坯加工方法 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09314278A (ja) * | 1996-05-30 | 1997-12-09 | Fukushima Seiko Kk | チタン・チタン合金鋳造用鋳型材 |
JP2007332420A (ja) * | 2006-06-15 | 2007-12-27 | Nippon Steel Corp | チタン材の製造方法および熱間圧延用素材 |
WO2014163087A1 (ja) * | 2013-04-01 | 2014-10-09 | 新日鐵住金株式会社 | 熱間圧延用チタン鋳片およびその製造方法 |
Family Cites Families (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6256561A (ja) * | 1985-09-06 | 1987-03-12 | Honda Motor Co Ltd | TiまたはTi合金の表面硬化方法 |
JPH0776431B2 (ja) * | 1987-12-11 | 1995-08-16 | 住友金属工業株式会社 | チタン製品の表面硬化方法 |
JPH05148598A (ja) * | 1991-02-20 | 1993-06-15 | Mitsubishi Materials Corp | チタン又はチタン合金からなる基材の表面硬化法および表面硬化部材 |
JPH04272147A (ja) * | 1991-02-25 | 1992-09-28 | Sumitomo Metal Ind Ltd | チタンの製造方法 |
JP2004115906A (ja) * | 2002-09-20 | 2004-04-15 | Ichiro Kawakatsu | TiまたはTi合金基体に対するAl−Si合金の被覆法 |
JP2007084855A (ja) * | 2005-09-20 | 2007-04-05 | Yamaha Motor Co Ltd | 黒色表面を有するチタン部材およびその製造方法 |
CN103348029B (zh) * | 2011-02-10 | 2016-03-30 | 新日铁住金株式会社 | 疲劳强度优异的耐磨损性钛合金构件 |
US10046373B2 (en) * | 2013-04-01 | 2018-08-14 | Nippon Steel & Sumitomo Metal Corporation | Titanium cast product for hot rolling and method for manufacturing same |
JP2014233753A (ja) * | 2013-06-05 | 2014-12-15 | 新日鐵住金株式会社 | 分塊工程や精整工程を省略しても熱間圧延後の表面性状に優れた工業用純チタンインゴットおよびその製造方法 |
-
2014
- 2014-09-30 UA UAA201702911A patent/UA116510C2/uk unknown
- 2014-09-30 EP EP14903243.5A patent/EP3202953A4/en not_active Withdrawn
- 2014-09-30 KR KR1020177008318A patent/KR20170047339A/ko not_active Application Discontinuation
- 2014-09-30 CN CN201480082171.1A patent/CN107075688B/zh active Active
- 2014-09-30 US US15/513,776 patent/US20170349973A1/en not_active Abandoned
- 2014-09-30 JP JP2014549247A patent/JP6075385B2/ja active Active
- 2014-09-30 EA EA201790491A patent/EA201790491A1/ru unknown
- 2014-09-30 WO PCT/JP2014/076083 patent/WO2016051502A1/ja active Application Filing
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09314278A (ja) * | 1996-05-30 | 1997-12-09 | Fukushima Seiko Kk | チタン・チタン合金鋳造用鋳型材 |
JP2007332420A (ja) * | 2006-06-15 | 2007-12-27 | Nippon Steel Corp | チタン材の製造方法および熱間圧延用素材 |
WO2014163087A1 (ja) * | 2013-04-01 | 2014-10-09 | 新日鐵住金株式会社 | 熱間圧延用チタン鋳片およびその製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3202953A4 * |
Also Published As
Publication number | Publication date |
---|---|
EP3202953A4 (en) | 2018-05-09 |
KR20170047339A (ko) | 2017-05-04 |
JPWO2016051502A1 (ja) | 2017-04-27 |
CN107075688A (zh) | 2017-08-18 |
UA116510C2 (uk) | 2018-03-26 |
EP3202953A1 (en) | 2017-08-09 |
JP6075385B2 (ja) | 2017-02-08 |
US20170349973A1 (en) | 2017-12-07 |
EA201790491A1 (ru) | 2017-07-31 |
CN107075688B (zh) | 2019-06-18 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
WO2014163087A1 (ja) | 熱間圧延用チタン鋳片およびその製造方法 | |
JP6521071B2 (ja) | 熱間圧延用チタン素材 | |
EP2982777A1 (en) | Titanium slab for hot rolling and method for manufacturing same | |
WO2014163086A1 (ja) | 熱間圧延用チタン鋳片およびその製造方法 | |
EP2700458B1 (en) | Titanium slab for hot rolling and process for producing same | |
JP6075384B2 (ja) | 熱間圧延用チタン鋳片およびその製造方法 | |
CN106715005B (zh) | 即使省略初轧工序、精整工序,热轧后的表面性状也优异的热轧用钛铸坯及其制造方法 | |
JP6075385B2 (ja) | 熱間圧延用チタン鋳片およびその製造方法 | |
JP6075387B2 (ja) | 表面疵の発生し難い熱間圧延用チタン鋳片およびその製造方法 | |
JP6171836B2 (ja) | 熱間圧延用チタン合金スラブおよびその製造方法 | |
WO2017018521A1 (ja) | 熱間圧延用チタン材 | |
KR101953487B1 (ko) | 표면 결함이 발생하기 어려운 열간 압연용 티타늄 주조편 및 그 제조 방법 | |
WO2016051482A1 (ja) | 熱間圧延用チタン鋳片およびその製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2014549247 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 14903243 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 15513776 Country of ref document: US |
|
ENP | Entry into the national phase |
Ref document number: 20177008318 Country of ref document: KR Kind code of ref document: A |
|
WWE | Wipo information: entry into national phase |
Ref document number: 201790491 Country of ref document: EA Ref document number: A201702911 Country of ref document: UA |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
REEP | Request for entry into the european phase |
Ref document number: 2014903243 Country of ref document: EP |