WO2010090310A1 - 電子ビーム溶解炉で溶製された熱間圧延用チタンスラブとその溶製方法および熱間圧延用チタンスラブの圧延方法 - Google Patents
電子ビーム溶解炉で溶製された熱間圧延用チタンスラブとその溶製方法および熱間圧延用チタンスラブの圧延方法 Download PDFInfo
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- WO2010090310A1 WO2010090310A1 PCT/JP2010/051786 JP2010051786W WO2010090310A1 WO 2010090310 A1 WO2010090310 A1 WO 2010090310A1 JP 2010051786 W JP2010051786 W JP 2010051786W WO 2010090310 A1 WO2010090310 A1 WO 2010090310A1
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- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims abstract description 156
- 239000010936 titanium Substances 0.000 title claims abstract description 154
- 229910052719 titanium Inorganic materials 0.000 title claims abstract description 154
- 238000002844 melting Methods 0.000 title claims abstract description 85
- 230000008018 melting Effects 0.000 title claims abstract description 85
- 238000010894 electron beam technology Methods 0.000 title claims abstract description 56
- 238000000034 method Methods 0.000 title claims abstract description 54
- 238000005098 hot rolling Methods 0.000 title claims description 83
- 229910052751 metal Inorganic materials 0.000 claims abstract description 32
- 239000002184 metal Substances 0.000 claims abstract description 32
- 238000005096 rolling process Methods 0.000 claims abstract description 32
- 238000005452 bending Methods 0.000 claims description 15
- 238000002347 injection Methods 0.000 claims description 11
- 239000007924 injection Substances 0.000 claims description 11
- 239000007790 solid phase Substances 0.000 claims description 10
- 230000002093 peripheral effect Effects 0.000 claims description 5
- 229910001069 Ti alloy Inorganic materials 0.000 claims description 4
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- 238000004519 manufacturing process Methods 0.000 abstract description 14
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- 230000015556 catabolic process Effects 0.000 abstract description 7
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- 239000000463 material Substances 0.000 description 10
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- 238000001816 cooling Methods 0.000 description 6
- 239000002994 raw material Substances 0.000 description 5
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- 238000010438 heat treatment Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
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- 230000000052 comparative effect Effects 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
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- 230000008023 solidification Effects 0.000 description 2
- 229910000756 V alloy Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- HIMLGVIQSDVUJQ-UHFFFAOYSA-N aluminum vanadium Chemical compound [Al].[V] HIMLGVIQSDVUJQ-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
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- 229910052786 argon Inorganic materials 0.000 description 1
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Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- 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
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/041—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for vertical casting
-
- 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
- B22D21/002—Castings of light metals
- B22D21/005—Castings of light metals with high melting point, e.g. Be 1280 degrees C, Ti 1725 degrees C
-
- 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
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21B—MANUFACTURE OF IRON OR STEEL
- C21B11/00—Making pig-iron other than in blast furnaces
- C21B11/10—Making pig-iron other than in blast furnaces in electric furnaces
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C1/00—Refining of pig-iron; Cast iron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
- B21B1/24—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 in a continuous or semi-continuous process
- B21B1/26—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 in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
-
- 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
- B21B1/42—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 step-by-step or planetary rolling
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12389—All metal or with adjacent metals having variation in thickness
Definitions
- the present invention relates to a titanium slab suitable for hot rolling produced by an electron beam melting furnace and a method for producing the same.
- Metallic titanium is in a state where manufacturers of sponge titanium or ingots are busy responding to increased production in response to an unprecedented increase in demand. This situation continues not only in sponge titanium or ingot manufacturers, but also in manufacturers that process the titanium ingots into forged plate materials.
- the conventional general manufacturing method of a strip coil which is a kind of plate material processed from a titanium ingot as described above, starts from a large titanium ingot melted and solidified by a consumable electrode arc melting method or an electron beam melting method. Then, this is broken down to produce a slab for hot rolling.
- This large ingot has a cylindrical shape with a diameter of about 1 m in the case of the consumable electrode type arc melting method, and a rectangular shape in the case of the electron beam melting method. Have Since it has such a large cross section, this large ingot is broken down by hot working such as ingots, forging and rolling, and has a slab shape that can be rolled by a hot rolling mill.
- the slab for hot rolling is heated to a predetermined temperature and hot-rolled by a general-purpose hot rolling mill such as steel and processed into a strip coil (thin plate).
- the hot-rolled strip coil is then annealed or descaled to become a product as it is, or further subjected to cold processing such as cold rolling and annealing to be a product.
- rectangular ingots are also made by making the cross-sectional shape of the mold rectangular.
- the thickness of the rectangular ingot is not melted so thin that it can be applied to a hot rolling mill without going through a breakdown process. Therefore, a technique for melting a thinner rectangular ingot is desired, but it has not yet been put into practical use.
- a dedicated mold for melting the titanium slab is required. Become.
- the thickness of the conventional rectangular mold is simply reduced when the titanium slab is melted in the electron beam melting furnace, warping and bending occur in the titanium slab melted in the mold, and the longitudinal direction
- it encounters a new problem that it cannot be directly fed into a general-purpose hot rolling mill used for rolling of steel and steel.
- Patent Document 1 A method for melting a rectangular ingot using a rectangular mold using an electron beam melting furnace is disclosed in, for example, Japanese Patent Application Laid-Open No. 04-131330 (Patent Document 1).
- FIG. 1 of Patent Document 1 shows a view in which the molten metal is poured from the long side mold wall side of the square mold 1.
- Patent Document 1 there is a description of the effect that the rolling process of the ingot can be improved by melting a rectangular ingot, but the bending of a titanium slab melted using a rectangular mold is not possible.
- linearity such as warpage.
- Patent Document 2 JP-A-62-050047 (Patent Document 2), the surface of a titanium slab drawn from a mold constituting an electron beam melting furnace is irradiated with an electron beam to melt and heat the surface layer portion, and then surface molding is performed.
- a method for improving the casting surface of a cast slab by manufacturing the slab on a rolling roll is disclosed.
- Patent Document 2 since a surface defect or a large oscillation mark is generated if the slab is simply pulled out from the mold, the surface layer portion is melted again by irradiating the electron beam and then applied to the surface forming roll.
- the example of the rectangular titanium slab which obtains a favorable casting surface by this and has a cross section of 180 mm x 50 mm is disclosed.
- Patent Document 2 there is no technical disclosure regarding linearity such as bending and warping of a titanium slab melted using a square mold.
- a large-scale hot rolling mill such as steel for manufacturing a strip coil has a large temperature drop and is not suitable.
- Patent Document 2 it is necessary to separately prepare an electron gun for heating a titanium slab inside the surface forming roll and the electron beam melting furnace after being pulled out from the mold, and there remains a problem in terms of cost.
- the present invention relates to a titanium slab having characteristics suitable for hot rolling, such that it can be fed into a hot rolling mill without undergoing a breakdown step or a subsequent correction step after melting by an electron beam melting furnace, and its The purpose is to provide a melting method.
- the above-mentioned problems have been intensively studied, and among the long-side mold wall and the short-side mold wall constituting the rectangular mold, the molten metal is injected from the short-side mold wall side so that a straight line in the longitudinal direction is obtained.
- the present inventors have found that a titanium slab excellent in properties can be melted, and have completed the present invention described below.
- the titanium slab for hot rolling according to the present invention is a titanium slab directly melted from a mold of an electron beam melting furnace, and the warp per 1000 mm of the length of the slab is 5 mm or less, and the bending is 2.5 mm or less. It is characterized by being.
- warp in the present invention means the maximum amount of deformation in the amount of deformation in the vertical direction (thickness direction) with respect to the longitudinal direction of the slab in the sectional view of the slab.
- the “bend” means the maximum deformation amount in the horizontal direction (width direction) with respect to the longitudinal direction of the slab in the plan view of the slab.
- the ratio (W / T) of the width (W) to the thickness (T) of the titanium slab is in the range of 2 to 10, and the length (L ) Ratio (L / W) is 5 or more.
- the titanium slab for hot rolling according to the present invention preferably has a thickness of 150 to 300 mm, a width of 1750 mm or less, and a length of 5000 mm or more.
- a chamfered portion having a radius of curvature (rc) of 5 to 50 mm is formed at a corner portion of the titanium slab for hot rolling according to the present invention.
- the titanium slab for hot rolling according to the present invention has a rectangular shape from a short side mold wall constituting a rectangular mold in which a molten titanium melted in a hearth disposed in an electron beam melting furnace is provided on the downstream side of the hearth.
- a preferred embodiment is that it is injected into a mold and melted.
- the titanium slab for hot rolling according to the present invention is preferably made of pure titanium or a titanium alloy.
- pure titanium means a JIS type 1 to type 4 equivalent product.
- the titanium alloy means a titanium material to which a metal element other than those prescribed for the pure titanium is intentionally added.
- the method for melting a titanium slab for hot rolling according to the present invention is a method in which a molten metal is poured from the short-side mold wall side among the long-side mold wall and the short-side mold wall constituting the rectangular mold built in the electron beam melting furnace. It is characterized by injecting.
- the short side mold facing the short side mold wall on the molten metal injection side with the electron beam density applied to the surface of the molten titanium pool formed in the rectangular mold. It is a preferred embodiment to decrease from the wall side toward the short side mold wall side on the molten metal injection side.
- a chamfered portion is formed at a corner portion of the rectangular mold, and a shape of the chamfered portion is formed inside the rectangular mold and an outer peripheral portion thereof. It is preferable to use a template formed so as to be similar to an equilibrium solid phase line that is a boundary with a solidified shell formed in the above.
- a chamfered portion is formed at a corner portion of the rectangular mold, the chamfered portion is constituted by a part of an arc, and a radius of curvature (rc) of the arc. It is preferable to use a mold having a thickness of 2 to 50 mm.
- the ratio (W / D) of the width (W) to the thickness (D) of the rectangular mold is in the range of 2 ⁇ (W / D) ⁇ 10. It is a preferred embodiment to use the template described above.
- the radius of curvature (rc) of the chamfered portion of the rectangular mold is proportional to the ratio ( ⁇ ) of the mold short side to the mold long side. It is a preferred embodiment to use a template configured as described above.
- the rolling method of the titanium slab for hot rolling according to the present invention is a preferred embodiment in which the hot slab is fed into a hot rolling mill and hot rolled into a strip coil.
- the rolling method of the titanium slab for hot rolling according to the present invention is a preferred embodiment in which the hot rolling is performed using a tandem rolling mill, a Steckel rolling mill, or a planetary rolling mill.
- the present invention since the warping and bending of the titanium slab are highly suppressed, there is no need for a breakdown step or a subsequent correction step after melting the electron beam, and such a length that can be fed into a hot rolling mill.
- the present invention provides a titanium slab for hot rolling excellent in directional linearity and a melting method thereof.
- the titanium slab manufactured by the above-described apparatus and method is excellent in linearity in the longitudinal direction, and as a result, stable hot rolling can be performed with a general-purpose hot rolling mill such as steel. Prior to this, it is possible to save labor in the breakdown process and the correction process in the longitudinal direction of the titanium slab, and as a result, the processing time of the titanium thin plate can be greatly shortened.
- FIG. 1 schematically shows the shape of a titanium slab for hot rolling according to the present invention. Further, FIG. 2 shows a warp in the longitudinal direction of the slab, and FIG.
- the titanium slab for hot rolling manufactured by the method of the present invention is first placed on a surface plate with a smooth surface and checked for warpage and bending. That is, the titanium slab is swung in the vertical direction to check the vertical deformation of the titanium slab, the distance between the corner of the other end floating from the surface plate and the surface plate is measured, and the maximum value among them Is measured as “warping” as shown in FIG.
- FIG. 4 shows a plan view of a rectangular mold for melting a titanium slab in an electron beam melting furnace.
- the rectangular mold has a long-side mold wall and a short-side mold wall, and in the present invention, it is preferable to inject molten metal from the short-side mold wall side as shown in FIG. 4 (a).
- the titanium slab excellent in linearity in the longitudinal direction can be melted.
- the linearity is such that the warp per 1000 mm length of the slab is 5 mm or less and the bend is 2.5 mm or less, and it is of a quality that can sufficiently ensure stable material passing properties with a general-purpose hot rolling mill such as steel.
- the molten metal is poured because the corner portion of the mold uses a thin mold. Very close to the place.
- the corner portion of the mold has a higher cooling ability than the flat portion, and has an effect of rapidly relieving a temperature difference caused by pouring the molten metal.
- the symmetry of cooling is enhanced and warping and bending are suppressed.
- the temperature distribution is symmetrical with respect to the opposing long side mold walls, and as a result, it is considered that the thin deformation in the thickness direction does not easily occur.
- the electron beam density applied to the surface of the molten titanium pool formed in the rectangular mold is set to one short side mold side facing the short side mold on the molten metal injection side. It is preferable to irradiate the electron beam so as to decrease toward the short side mold wall side on the molten metal injection side.
- the temperature is high at the short side mold wall on the molten metal injection side and the temperature is lowered because there is a distance at the opposing short side mold wall, the molten titanium pool in the rectangular mold with the electron beam irradiation pattern as described above Is heated, the temperature distribution in the width direction of the titanium slab can be maintained uniformly. As a result, there is an effect that deformation of the molten titanium slab can be further effectively suppressed.
- the titanium slab for hot rolling manufactured by the apparatus and method employing the electron beam pattern according to the present invention has a warp per slab length of 1000 mm of 5 mm or less, a bend of 2.5 mm or less, Preferably, the warpage can be controlled to 2 mm or less and the bending can be controlled to 2 mm or less, and the material permeability during hot rolling can be further stabilized.
- the titanium slab for hot rolling according to the present invention is characterized by being directly melted from an electron beam melting furnace. Since the titanium slab has been adjusted to a thickness suitable for rolling from the beginning of melting, a titanium slab not only does not require a breakdown process to a slab that has been performed from a conventional ingot, but also remains as a molten titanium slab. Since the warpage and bending are extremely small, it is possible to eliminate the need for machining by a correction process or cutting.
- a titanium slab according to the present invention is a titanium slab for hot rolling manufactured directly from an electron beam melting furnace, and a ratio (W / T) of a width (W) to a thickness (T) of the titanium slab is 2
- the preferred embodiment is that the ratio (L / W) of the length (L) to the width is 5 or more in the range of ⁇ 10.
- the thickness (T) of the titanium slab is 150 to 300 mm
- the width (W) is 1750 mm or less
- the length (L) is preferably 5000 mm or more, more preferably 5600 mm or more, more preferably 6000 mm or more, and further It is more preferable to select from a range of 7000 mm or more.
- the ratio (W / T) of the width (W) to the thickness (T) of the titanium slab is less than 2, the titanium slab is thick with respect to the width, so that the width expansion during hot rolling becomes large. The edge part is cracked, which is not preferable.
- the thickness exceeds 300 mm, the free surface at the time of hot rolling becomes large, the side surface becomes deep, and cracking of the edge portion is promoted.
- the thickness of the titanium slab is less than 150 mm, the temperature of the slab is greatly lowered during hot rolling, which may impair material penetration and may cause edge cracking. Moreover, at the time of casting of a slab, linearity cannot be maintained by the weight of the titanium slab itself, and it becomes difficult to continue melting the titanium slab smoothly. (Refer to the main apparatus configuration of a suitable electron beam melting furnace shown in FIG. 5 described later.)
- the W / T of the titanium slab exceeds 10
- the thickness of the slab pulled out from the mold becomes too thin, and there is a problem that sufficient strength required for pulling out cannot be obtained. If the thickness of the titanium slab exceeds 300 mm or the width exceeds 1750 mm, the rolling load of hot rolling increases, and a general-purpose hot rolling mill cannot perform direct rolling, which is contrary to the purpose of the present application.
- the titanium slab for hot rolling according to the present invention is the production efficiency when melting the hot rolling slab in an electron beam melting furnace, when rolling into a strip coil with a general-purpose hot rolling mill such as steel.
- the ratio (L / W) of the length (L) and the width (W) of the titanium slab for hot rolling is 5 or more, and the length of the slab is preferably 5000 mm or more, If the L / W of the slab is small and the length is short, the density of titanium is as light as 60% of that of steel, so the slab will flutter easily due to the reaction from the transport roller, etc. May occur.
- the length is shorter than 5000 mm, it is difficult to engage with the roll of the next stage when hot rolling the strip coil, which is not preferable.
- L / W is preferably 5 or more.
- FIG. 6 is a view of the mold 3 in FIG. 5 as viewed from above.
- a chamfered portion is formed at the corner portion of the rectangular mold 31, and the shape of the chamfered portion is formed in the molten metal 32 formed in the rectangular mold and the outer peripheral portion thereof. It is preferable to use a template formed so as to be similar to the equilibrium solid phase line 35 that is a boundary with the solidified shell 34.
- the equilibrium solid phase line 35 indicates a boundary surface between the solid phase 34 and the liquid phase 32 formed inside the rectangular mold 31 and corresponds to a line connecting temperatures corresponding to the solidification point of the molten metal.
- solid and liquid coexist at the melting point of the metal, but the outer peripheral surface of the mold pool 32 represents a solid phase.
- this isotherm is called an equilibrium solid phase line 35.
- the equilibrium solid phase line 35 forms a straight line parallel to the mold wall at the long and short sides of the mold.
- the corner portion is composed of an outwardly convex curve.
- the shape of the curve and it is preferable that the shape of the corner portion of the rectangular mold 31 is configured to be similar to the equilibrium solid phase line 35 formed in the rectangular mold 31. It is said.
- a heat flow due to heat removal from the mold pool 32 to the water-cooled mold 31 is formed in a direction perpendicular to the mold inner surface.
- the cast structure formed in this way is also formed along the heat flow, and has the effect of melting an ingot with a uniform solidified structure.
- the chamfered portion of the corner portion of the rectangular mold 31 can be configured as a part of an arc.
- the radius of curvature (rc) of the arc of the chamfered portion is preferably set in the range of 2 to 50 mm.
- the radius of curvature of the arc constituting the chamfered portion of the corner portion exceeds the upper limit value of 50 mm, the solidified structure of the corner portion of the titanium slab to be melted is maintained healthy, but the titanium slab is formed by rolling. The homogeneity of the thin plate is lowered, which is not preferable. Further, the cooling and solidification rate of the slab corner portion is lowered, and there is concern about breakout from the slab, which is not preferable.
- a chamfered portion having a radius of curvature smaller than the lower limit 2 mm of the radius of curvature is configured, heat removal from the slab to the mold corner is large, and it is difficult to enjoy the effect of improving the slab surface casting surface. Cracks and scratches are generated at the corners of the manufactured titanium slab itself, which is not preferable.
- the radius of curvature of the arc constituting the chamfered portion of the corner portion of the rectangular mold 31 is preferably set in the range of 2 to 50 mm, more preferably 5 to 30 mm.
- the radius of curvature (rc) of the chamfered portion is proportional to the ratio ( ⁇ ) of the length of the mold short side to the length of the mold long side. That is, it is preferable that the chamfered portion be configured to be larger as the thickness of the ingot to be melted increases.
- the ratio (W / D) of the width (W) to the thickness (D) of the mold used in the present invention is preferably in the range of 2 ⁇ (W / D) ⁇ 10, and more preferably 2.5 ⁇ ( W / D) ⁇ 8 is more preferable.
- the shape of the mold used in the present invention is preferably a square, and the thickness of the mold is preferably thinner with respect to the rolling process used in the subsequent process.
- the amount of heat removed to the water-cooled copper wall increases as the mold thickness decreases, it is necessary to increase the amount of heat supplied to the mold pool.
- the size of the mold has an upper limit and a lower limit, and in the present invention, as a result of various studies, the ratio of the width to the thickness of the mold (W / D) is set to 10 as the upper limit. If the mold width is shortened beyond the upper limit, the amount of heat removed from the mold pool to the mold increases, and the amount of electron beam heating corresponding to this increases, which is not preferable. On the other hand, if the ratio (W / D) is less than or equal to the lower limit of 2, the cross section approaches a square and the relationship between the width and thickness of the mold becomes close, and the effect of the present invention cannot be obtained. Further, if it is 1 or less, the relationship between the width and the thickness is reversed and does not make sense of the present invention.
- the ratio of the width to the thickness of the mold (W / D) is more preferably set to 2.5 to 8, so that the slab having the desired width and thickness can be obtained even when the mold is slightly deformed. The effect of being able to reliably melt is produced.
- the shape of the electron beam is also formed in a circle, and the radius of the circle is made to coincide with the radius of curvature of the arc constituting the chamfered portion. It is preferable.
- the titanium slab described above can be made of either pure titanium or a titanium alloy.
- the present invention can also be applied to a titanium slab made by melting sponge titanium as a raw material or a titanium slab made by adding an alloy component to sponge titanium.
- FIG. 5 shows a main apparatus configuration of an electron beam melting furnace suitable for melting a titanium slab according to the present invention.
- the titanium raw material 10 charged into the hearth 4 is heated and melted by the electron beam 2 emitted from the electron gun 1 held at the top of the electron beam melting furnace to generate the molten metal 5.
- the molten metal 5 continuously poured into the mold 3 is united with the titanium pool 6 formed inside the mold 3, and the titanium slab 7 solidified below the titanium pool 6 is continuously pulled out,
- the titanium pool surface 6 is operated to keep it at a certain level.
- the aforementioned hearth 4 and mold 3 are housed in the melting chamber 11 and shielded from the atmosphere, and the inside of the melting chamber 11 is maintained at a reduced pressure.
- the titanium slab 7 drawn out from the lower end of the mold 3 is continuously drawn out into the ingot chamber 12 disposed in close contact with the lower portion of the melting chamber 11.
- the inside of the ingot chamber 12 is preferably maintained in a reduced pressure state like the melting chamber 11.
- the titanium slab 7 drawn out into the ingot chamber 12 by a predetermined amount is preferably pulled out from the mold 3 and then the gate valve 20 is operated to cut the edge between the melting chamber 11 and the ingot chamber 12.
- the titanium slab 7 cooled to room temperature can be extracted into the atmosphere from an open door (not shown) provided in the ingot chamber 12.
- the length of the ingot chamber 12 is preferably secured at least 5000 mm.
- the mold 3 is preferably configured to have a thickness suitable for melting the titanium slab 7 described above, and specifically, it is preferably configured in the range of 150 to 300 mm.
- the ratio (W / T) of the width (W) to the thickness (T) of the rectangular mold is preferably in the range of 2 to 10.
- the titanium slab extracted from the electron beam melting furnace shown in FIG. 5 is then removed from the deposits and irregularities formed on the surface by cutting or polishing, heated in a heating furnace, and then heated to a high temperature.
- a hot rolling mill By feeding into a hot rolling mill in a state, it can be hot-rolled into a strip coil.
- a tandem rolling mill In the present invention, a tandem rolling mill, a stickel rolling mill, or a planetary rolling mill can be suitably used as the rolling mill.
- the tandem rolling mill can be suitably used during rough rolling to finish rolling when hot rolling a titanium slab into a strip coil.
- the titanium slab melted by the electron beam melting furnace described above can suitably use a hot rolling mill owned by a steel manufacturer, and as a result, can produce a hot rolled titanium coil with excellent quality. Some have the effect of being able to.
- Example 1 Melting raw material: sponge titanium2. Melting device: 1) Electron beam output Hearth side: 1000 kW at maximum Mold side: Max 400kW 2) Square mold Size: Thickness 270mm x Width 1100mm Structure: Water-cooled copper 3) Melt injection direction into mold: Injection from short side mold of square mold
- a total of five titanium slabs having a width of 1100 mm, a thickness of 270 mm, and lengths of 5600, 6000, 7000, 8000, and 9000 mm were melted using the above-described apparatus configuration and raw materials.
- the warp and bend in the longitudinal direction of the melted titanium slab are measured by the above method.
- the warp per slab length of 1000 mm is 0.5 to 4 mm, and the bend is 0.5 to 2 mm. It had sufficient linearity to run on a hot rolling mill.
- the electron beam density is decreased from the short side mold wall facing the short side mold wall into which the molten metal is injected in the width direction of the rectangular mold, and the rectangular mold pool surface temperature is reduced. It melt
- Example 3 After cutting and cleaning the cast surface of the titanium slab melted in Example 1, the titanium slab was subjected to a steel hot rolling mill to obtain a strip coil having a thickness of 3 to 6 mm. Further, the strip coil can be shot blasted and washed with nitric hydrofluoric acid, and after descaling, a thin plate having a thickness of 0.3 to 1 mm can be efficiently produced by cold rolling. It was.
- Example 4 In Example 1, 1100 mm in width, 270 mm in thickness, and 5600 in length under the same conditions except that an aluminum-vanadium alloy was added to titanium sponge and a slab of 3Al-2.5V (JIS 61 type) alloy was melted. , 6000, 7000, 8000 and 9000 mm in total, 5 titanium slabs were melted. The molten titanium slab had sufficient linearity to be subjected to a hot rolling mill.
- Example 5 Pure titanium slabs were melted using a mold in which the cross-sectional shape of the corner as shown in FIG. 6 was formed along a figure similar to the equilibrium solidus.
- the surface of the slab after melting was investigated, the solidified structure was sound and cracks and the like were not observed.
- the surface layer of the slab was cut by 1 mm and rolled as it was to produce a thin plate, but no cracks or surface defects were observed.
- the slab yield after surface cutting was 98%.
- Example 1 In Example 1, a titanium slab was melted under the same conditions except that the molten metal was poured from the long side mold direction constituting the rectangular mold. As a result, although the titanium slab of a predetermined length could be smoothly melted, the warp per 1000 mm length was 6-15 mm and the bend was 3-5 mm, and it was sent to the hot rolling mill as it is. I could't. Therefore, after ensuring linearity by using a straightening machine, a thin coil was obtained by using a rolling mill.
- Example 2 A titanium slab was melted by using a conventional mold having a square inner surface instead of the mold having a curved corner portion used in Example 5. As a result, the casting surface of the parallel part of the melted slab was sound, but the casting surface was rough at the corner, and minute cracks were also observed. As a result, the surface layer portion was ground by 5 mm and rolled to produce a thin plate. No cracks or surface flaws were observed on the manufactured thin plate. However, the cutting yield was reduced to 95% by the surface grinding performed prior to rolling.
- a high-quality titanium slab can be directly melted using an electron beam melting furnace, which contributes to a reduction in manufacturing costs of titanium products.
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Abstract
Description
図1は、本願発明に係る熱間圧延用チタンスラブの形状を模式的に表している。また、図2はスラブの長手方向の反りを、図3はスラブの長手方向の曲がり(キャンバー)を説明する図を示している。
1.溶解原料:スポンジチタン
2.溶解装置:
1)電子ビーム出力
ハース側:最大1000kW
鋳型側:最大400kW
2)角形鋳型
大きさ:厚み270mm×幅1100mm
構成:水冷銅
3)鋳型への溶湯注入方向:角形鋳型の短辺鋳型から注入
実施例1の条件に加えて、矩形鋳型の幅方向に対して、溶湯の注入した短辺鋳型壁に向かって対向する短辺鋳型壁から電子ビーム密度を減少させて、矩形鋳型プール表面温度を均一に保持して溶解を行った。その結果、溶製されたチタンスラブの反りと曲がりは、いずれも安定して小さくなり、反りが2mm以下となった。
実施例1で溶製されたチタンスラブの鋳肌の切削手入れした後、前記チタンスラブを鉄鋼の熱間圧延機にかけて、厚さ3~6mmの帯状コイルを得た。更に、前記帯状コイルを、ショットブラスト、硝フッ酸酸洗することで、脱スケールした後、冷間圧延によって最終的には、厚さ0.3~1mmの薄板を効率よく製造することができた。
実施例1において、スポンジチタンにアルミーバナジウム合金を添加して、3Al-2.5V(JIS61種)合金のスラブを溶製した以外は同じ条件下にて、幅1100mm、厚み270mm、長さ5600、6000、7000、8000および9000mmの計5本のチタンスラブを溶製した。溶製されたチタンスラブは、熱間圧延機にかけるに十分な直線性を有していた。
図6に示したようなコーナー部の断面形状を平衡固相線に相似な図形に沿って形成した鋳型を用いて純チタンスラブを溶製した。溶製後のスラブの表面を調査したところ、凝固組織は健全であり、しかも割れ等の生成は認められなかった。ただし、念のため、前記スラブの表層部を1mmだけ切削して、そのまま圧延して薄板を製造したが、割れや表面疵等の発生は見られなかった。 なお、表面切削後のスラブの歩留まりは、98%であった。
実施例1において、角形鋳型を構成する長辺鋳型方向から溶湯を注入した以外は同じ条件下でチタンスラブを溶製した。その結果、順調に所定長さのチタンスラブを溶製することができたものの、長さ1000mm当たりの反りが6~15mm、曲がりが3~5mmもあり、そのままでは熱間圧延機に送入することができなかった。そこで、矯正機にかけて直線性を担保した後、圧延機にかけて薄板コイルを得た。
実施例5において用いたコーナー部を曲面で構成した鋳型の代わりに、内面も角形の従来の鋳型を用いてチタンスラブを溶製した。その結果、溶製されたスラブの平行部の鋳肌は健全であったが、コーナー部においては、鋳肌が荒れており、また微小なクラックも観察された。その結果、表層部を5mmだけ研削して、圧延し、薄板を製造した。製造された薄板には割れや表面疵等の発生は見られなかった。ただし、圧延に先立って行った表面研削により、切削歩留まりは95%に低下した。
Claims (13)
- 電子ビーム溶解炉の鋳型から直接溶製されたチタンスラブであって、スラブの長さ1000mm当たりの反り(長手方向に対する厚み方向の変形量)が5mm以下、曲がり(長手方向に対する幅方向の変形量)が2.5mm以下であることを特徴とする熱間圧延用チタンスラブ。
- 前記熱間圧延用チタンスラブの厚み(T)に対する幅(W)の比(W/T)が2~10の範囲であり、且つ、幅に対する長さ(L)の比(L/W)が5以上であることを特徴とする請求項1に記載の熱間圧延用チタンスラブ。
- 前記熱間圧延用チタンスラブの厚みが150~300mm、幅が1750mm以下、長さが5000mm以上であることを特徴とする請求項2に記載の熱間圧延用チタンスラブ。
- 前記熱間圧延用チタンスラブのコーナー部に、5~50mmの曲率半径(rc)を有する面取り部が形成されていることを特徴とする請求項1に記載の熱間圧延用チタンスラブ。
- 前記熱間圧延用チタンスラブが、純チタンまたはチタン合金で構成されていることを特徴とする請求項1~4のいずれかに記載の熱間圧延用チタンスラブ。
- 電子ビーム溶解炉を用いた熱間圧延用チタンスラブの溶製方法であって、前記電子ビーム溶解炉に内装された矩形鋳型を構成する長辺鋳型壁および短辺鋳型壁のうち、短辺鋳型壁側から溶湯を注入することを特徴とする熱間圧延用チタンスラブの溶製方法。
- 前記矩形鋳型内に形成された溶融チタンプール表面に照射する電子ビーム密度を、溶湯注入側の短辺鋳型と対向する短辺鋳型壁側から溶湯注入側の短辺鋳型壁側に向かって減少させることを特徴とする請求項6に記載の熱間圧延用チタンスラブの溶製方法。
- 前記矩形鋳型のコーナー部に面取り部を形成させ、前記面取り部の形状が矩形鋳型の内部に形成されている溶湯とその外周部に形成される凝固シェルとの境界である平衡固相線と相似となるように形成された鋳型を用いることを特徴とする請求項6または7に記載の熱間圧延用チタンスラブの溶製方法。
- 前記矩形鋳型のコーナー部に面取り部を形成させ、前記面取り部を円弧の一部で構成し、前記円弧の曲率半径(rc)が2~50mmとされた鋳型を用いることを特徴とする請求項6または7に記載の熱間圧延用チタンスラブの溶製方法。
- 前記矩形鋳型の厚み(D)に対する幅(W)の比(W/D)は、2≦(W/D)≦10の範囲とされた鋳型を用いることを特徴とする請求項6~9のいずれかに記載の熱間圧延用チタンスラブの溶製方法。
- 前記矩形鋳型の面取り部の曲率半径(rc)は、鋳型長辺に対する鋳型短辺の比(α)に対して比例関係となるように構成された鋳型を用いることを特徴とする請求項6~10のいずれかに記載の熱間圧延用チタンスラブの溶製方法。
- 請求項1~5のいずれかに記載の熱間圧延用チタンスラブを、熱間圧延機に送り込み、帯状コイルへ熱間圧延することを特徴とする熱間圧延用チタンスラブの圧延方法。
- 前記圧延機が、タンデム圧延機、ステッケル圧延機またはプラネタリー圧延機であることを特徴とする請求項12に記載の熱間圧延用チタンスラブの圧延方法。
Priority Applications (11)
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EP10738638.5A EP2394757B1 (en) | 2009-02-09 | 2010-02-08 | Process for the production of a titanium slab for hot rolling produced by electron-beam melting furnace |
CN2010800071064A CN102307686B (zh) | 2009-02-09 | 2010-02-08 | 用电子束熔化炉熔炼的热轧用钛板坯和其熔炼方法以及热轧用钛板坯的轧制方法 |
RU2011137130/02A RU2552209C2 (ru) | 2009-02-09 | 2010-02-08 | Титановый сляб для горячей прокатки, произведенный с помощью электронно-лучевой плавильной печи, процесс его производства и процесс прокатки титанового сляба для горячей прокатки |
JP2010549531A JP5119505B2 (ja) | 2009-02-09 | 2010-02-08 | 電子ビーム溶解炉で溶製された熱間圧延用チタンスラブとその溶製方法 |
KR1020177007767A KR20170036810A (ko) | 2009-02-09 | 2010-02-08 | 전자빔 용해로에서 용제된 열간 압연용 티탄 슬래브와 그 용제 방법 및 열간 압연용 티탄 슬래브의 압연 방법 |
AU2010211605A AU2010211605A1 (en) | 2009-02-09 | 2010-02-08 | Titanium slab for hot rolling produced by electron-beam melting furnace, process for production thereof, and process for rolling titanium slab for hot rolling |
CA2751697A CA2751697A1 (en) | 2009-02-09 | 2010-02-08 | Titanium slab for hot rolling produced by electron-beam melting furnace, process for production thereof, and process for rolling titanium slab for hot rolling |
US13/148,392 US9962760B2 (en) | 2009-02-09 | 2010-02-08 | Titanium slab for hot rolling produced by electron-beam melting furnace, process for production thereof, and process for rolling titanium slab for hot rolling |
SG2011055795A SG173514A1 (en) | 2009-02-09 | 2010-02-08 | Titanium slab for hot rolling produced by electron-beam melting furnace, process for production thereof, and process for rolling titanium slam for hot rolling |
BRPI1008184A BRPI1008184A2 (pt) | 2009-02-09 | 2010-02-08 | " placa de titânio para a laminação a quente produzida por forno de fundição por feixe de elétrons, processo para produção da mesma e processo para a laminação da placa de titânio para a laminação a quente" |
UAA201110737A UA107565C2 (uk) | 2009-02-09 | 2010-08-02 | Титановий сляб для гарячого вальцювання, одержаний за допомогою електронно-променевої печі, спосіб його виготовлення та спосіб вальцювання титанового сляба |
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CN (1) | CN102307686B (ja) |
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Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2013081980A (ja) * | 2011-10-07 | 2013-05-09 | Kobe Steel Ltd | チタンまたはチタン合金からなるスラブの連続鋳造方法および連続鋳造装置 |
JP2013107130A (ja) * | 2011-11-24 | 2013-06-06 | Toho Titanium Co Ltd | 熱間圧延用チタンスラブの溶製方法 |
JP2014018829A (ja) * | 2012-07-18 | 2014-02-03 | Toho Titanium Co Ltd | スラブの溶製方法および溶製装置 |
Families Citing this family (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5168434B2 (ja) * | 2011-04-22 | 2013-03-21 | 新日鐵住金株式会社 | 熱間圧延用チタンスラブおよびその製造方法 |
JP5896811B2 (ja) * | 2012-04-02 | 2016-03-30 | 株式会社神戸製鋼所 | チタンまたはチタン合金からなる鋳塊の連続鋳造用の鋳型およびこれを備えた連続鋳造装置 |
JP6611331B2 (ja) * | 2016-01-07 | 2019-11-27 | 株式会社神戸製鋼所 | チタンまたはチタン合金からなるスラブの連続鋳造方法 |
TWI626339B (zh) * | 2016-12-23 | 2018-06-11 | Nat Chung Shan Inst Science & Tech | Vacuum refining furnace device combining electron beam and region melting |
RU2745920C1 (ru) * | 2020-06-23 | 2021-04-02 | Акционерное общество «ЕВРАЗ НТМК Нижнетагильский металлургический комбинат» (АО «ЕВРАЗ НТМК») | Способ производства проката прямоугольного сечения из некондиционного проката круглого сечения |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6250047A (ja) | 1985-08-29 | 1987-03-04 | Kobe Steel Ltd | 連続鋳造方法 |
JPS62284049A (ja) * | 1986-06-02 | 1987-12-09 | Nippon Steel Corp | 熱間圧延用のチタン合金スラブ |
JPH04131330A (ja) | 1990-09-21 | 1992-05-06 | Nikko Kyodo Co Ltd | 純チタン又はチタン合金材の製造方法 |
JPH04319044A (ja) | 1991-02-06 | 1992-11-10 | Concast Service Union Ag | 連続鋳造鋳型 |
JPH08104961A (ja) * | 1994-10-05 | 1996-04-23 | Nkk Corp | 工業用純チタンの熱延板の製造方法 |
JPH1128550A (ja) | 1997-07-08 | 1999-02-02 | Sumitomo Metal Ind Ltd | 連続鋳造用鋳型及び連続鋳造時の幅替え方法 |
JPH11108556A (ja) * | 1997-08-04 | 1999-04-23 | Oregon Metallurg Corp | チタン精錬用ストレート炉床式炉 |
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 |
Family Cites Families (19)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CH424102A (de) * | 1965-05-03 | 1966-11-15 | Wertli Alfred | Verfahren zum Stranggiessen eines Bandes und Kühlvorrichtung zum Durchführen des Verfahrens |
US3764297A (en) * | 1971-08-18 | 1973-10-09 | Airco Inc | Method and apparatus for purifying metal |
US4168185A (en) * | 1977-02-25 | 1979-09-18 | Kobe Steel, Ltd. | Production method of titanium hot coil by continuous hot rolling system |
JPS5939202B2 (ja) * | 1979-04-26 | 1984-09-21 | 川崎製鉄株式会社 | 厚板の耳割れ防止方法 |
JPS6277427A (ja) * | 1985-09-30 | 1987-04-09 | Kobe Steel Ltd | 電子ビ−ム溶解・鋳造装置 |
US5224534A (en) | 1990-09-21 | 1993-07-06 | Nippon Mining And Metals Company, Limited | Method of producing refractory metal or alloy materials |
JP2662467B2 (ja) | 1991-03-13 | 1997-10-15 | 新日本製鐵株式会社 | ベルト式連続鋳造の注入方法 |
US5273101A (en) | 1991-06-05 | 1993-12-28 | General Electric Company | Method and apparatus for casting an arc melted metallic material in ingot form |
US5273102A (en) * | 1991-06-05 | 1993-12-28 | General Electric Company | Method and apparatus for casting an electron beam melted metallic material in ingot form |
RU2052534C1 (ru) * | 1993-11-09 | 1996-01-20 | Всерхнесалдинское металлургическое производственное объединение | СПОСОБ ИЗГОТОВЛЕНИЯ ЛИСТОВ ИЗ ТИТАНОВЫХ β -СПЛАВОВ |
CA2192834C (en) * | 1995-04-14 | 2001-02-13 | Shinichi Teraoka | Apparatus for producing strip of stainless steel |
KR100217943B1 (ko) | 1995-11-29 | 1999-09-01 | 이구택 | 심가공성이 우수한 냉연강판의 제조방법 |
UA56194C2 (uk) | 1999-05-18 | 2003-05-15 | Інститут електрозварювання ім .Є О. Патона Hаціональної Академії Hаук України | Спосіб одержання тонкого листа в установках електронно - променевого переплаву |
DE19960362C1 (de) | 1999-12-14 | 2001-05-10 | Ald Vacuum Techn Ag | Verfahren und Vorrichtung zum Herstellen von Stranggußblöcken aus Titanlegierungen |
US6561259B2 (en) * | 2000-12-27 | 2003-05-13 | Rmi Titanium Company | Method of melting titanium and other metals and alloys by plasma arc or electron beam |
NL1018817C2 (nl) * | 2001-08-24 | 2003-02-25 | Corus Technology B V | Werkwijze voor het bewerken van een continu gegoten metalen plak of band, en aldus vervaardigde plaat of band. |
US6868896B2 (en) | 2002-09-20 | 2005-03-22 | Edward Scott Jackson | Method and apparatus for melting titanium using a combination of plasma torches and direct arc electrodes |
ATE392280T1 (de) * | 2004-12-29 | 2008-05-15 | Concast Ag | Stahlstranggiessanlage für knüppel- und vorblockformate |
JP4443430B2 (ja) * | 2005-01-25 | 2010-03-31 | 東邦チタニウム株式会社 | 電子ビーム溶解装置 |
-
2010
- 2010-02-08 WO PCT/JP2010/051786 patent/WO2010090310A1/ja active Application Filing
- 2010-02-08 AU AU2010211605A patent/AU2010211605A1/en not_active Abandoned
- 2010-02-08 KR KR1020177007767A patent/KR20170036810A/ko not_active Application Discontinuation
- 2010-02-08 EP EP10738638.5A patent/EP2394757B1/en active Active
- 2010-02-08 KR KR1020117020209A patent/KR20110113195A/ko active Application Filing
- 2010-02-08 CN CN2010800071064A patent/CN102307686B/zh active Active
- 2010-02-08 CA CA2751697A patent/CA2751697A1/en not_active Abandoned
- 2010-02-08 JP JP2010549531A patent/JP5119505B2/ja active Active
- 2010-02-08 SG SG2011055795A patent/SG173514A1/en unknown
- 2010-02-08 US US13/148,392 patent/US9962760B2/en active Active
- 2010-02-08 RU RU2011137130/02A patent/RU2552209C2/ru active
- 2010-02-08 BR BRPI1008184A patent/BRPI1008184A2/pt not_active Application Discontinuation
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6250047A (ja) | 1985-08-29 | 1987-03-04 | Kobe Steel Ltd | 連続鋳造方法 |
JPS62284049A (ja) * | 1986-06-02 | 1987-12-09 | Nippon Steel Corp | 熱間圧延用のチタン合金スラブ |
JPH04131330A (ja) | 1990-09-21 | 1992-05-06 | Nikko Kyodo Co Ltd | 純チタン又はチタン合金材の製造方法 |
JPH04319044A (ja) | 1991-02-06 | 1992-11-10 | Concast Service Union Ag | 連続鋳造鋳型 |
JPH08104961A (ja) * | 1994-10-05 | 1996-04-23 | Nkk Corp | 工業用純チタンの熱延板の製造方法 |
JPH1128550A (ja) | 1997-07-08 | 1999-02-02 | Sumitomo Metal Ind Ltd | 連続鋳造用鋳型及び連続鋳造時の幅替え方法 |
JPH11108556A (ja) * | 1997-08-04 | 1999-04-23 | Oregon Metallurg Corp | チタン精錬用ストレート炉床式炉 |
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 |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2013081980A (ja) * | 2011-10-07 | 2013-05-09 | Kobe Steel Ltd | チタンまたはチタン合金からなるスラブの連続鋳造方法および連続鋳造装置 |
JP2013107130A (ja) * | 2011-11-24 | 2013-06-06 | Toho Titanium Co Ltd | 熱間圧延用チタンスラブの溶製方法 |
JP2014018829A (ja) * | 2012-07-18 | 2014-02-03 | Toho Titanium Co Ltd | スラブの溶製方法および溶製装置 |
Also Published As
Publication number | Publication date |
---|---|
EP2394757A1 (en) | 2011-12-14 |
CA2751697A1 (en) | 2010-08-12 |
CN102307686B (zh) | 2013-12-18 |
RU2552209C2 (ru) | 2015-06-10 |
CN102307686A (zh) | 2012-01-04 |
EP2394757A4 (en) | 2014-05-21 |
US20110308291A1 (en) | 2011-12-22 |
BRPI1008184A2 (pt) | 2016-03-01 |
SG173514A1 (en) | 2011-09-29 |
JPWO2010090310A1 (ja) | 2012-08-09 |
JP5119505B2 (ja) | 2013-01-16 |
KR20110113195A (ko) | 2011-10-14 |
KR20170036810A (ko) | 2017-04-03 |
US9962760B2 (en) | 2018-05-08 |
EP2394757B1 (en) | 2018-12-12 |
AU2010211605A1 (en) | 2011-08-25 |
RU2011137130A (ru) | 2013-03-20 |
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