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WO2017018454A1 - Brame en titane pour traitement de fusion de surface et matériau en titane pour laminage à chaud utilisant ladite brame - Google Patents

Brame en titane pour traitement de fusion de surface et matériau en titane pour laminage à chaud utilisant ladite brame Download PDF

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Publication number
WO2017018454A1
WO2017018454A1 PCT/JP2016/072040 JP2016072040W WO2017018454A1 WO 2017018454 A1 WO2017018454 A1 WO 2017018454A1 JP 2016072040 W JP2016072040 W JP 2016072040W WO 2017018454 A1 WO2017018454 A1 WO 2017018454A1
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WIPO (PCT)
Prior art keywords
slab
oxygen concentration
titanium
layer
melting treatment
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2016/072040
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English (en)
Japanese (ja)
Inventor
藤井　秀樹
知徳 國枝
吉紹 立澤
一浩 ▲高▼橋
森　健一
武士 三戸
圭介 諸富
洋介 井上
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Toho Titanium Co Ltd
Original Assignee
Toho Titanium Co Ltd
Nippon Steel and Sumitomo Metal Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Toho Titanium Co Ltd, Nippon Steel and Sumitomo Metal Corp filed Critical Toho Titanium Co Ltd
Priority to JP2016575693A priority Critical patent/JP6324549B2/ja
Priority to CN201680031125.8A priority patent/CN107614153B/zh
Publication of WO2017018454A1 publication Critical patent/WO2017018454A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • 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
    • 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
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K15/00—Electron-beam welding or cutting
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon

Definitions

  • the present invention relates to a titanium slab for surface melting treatment made of pure industrial titanium, and a titanium material for hot rolling in which the surface melting treatment is applied to the slab.
  • pure titanium for industrial use is made of sponge titanium or titanium scrap obtained by the crawl method, and uses high-density thermal energy sources such as vacuum arc melting (VAR), electron beam melting (EBR), or plasma arc melting. It was usual to melt
  • the shape of the slab is limited to a cylindrical slab (billet) in the case of vacuum arc melting, while it is cast into a rectangular slab, that is, a slab in the case of electron beam melting or plasma arc melting. Can do.
  • the surface of the large slab is subjected to surface cutting as necessary, and then subjected to hot rolling or forging, and then In general, it is processed into a hot rolling material having a shape and size suitable for hot rolling.
  • the hot working process by these block rolling or forging is referred to herein as a breakdown process.
  • the oxide layer and oxygen-enriched layer formed in the surface layer of the material for hot rolling after breakdown after cutting the surface layer to about several mm or more to nearly 10 mm by cutting, It was usual to use for hot rolling.
  • a DC (direct cast) slab casting technique is used as a method for producing a relatively thin slab-like slab, that is, a slab having a shape and size that can be directly subjected to hot rolling, in place of large-sized ingot casting.
  • molten titanium melted in a hearth by electron beam melting or plasma arc melting is continuously injected into a water-cooled copper mold of a predetermined shape held in a vacuum or an inert gas atmosphere, and
  • a solidified portion in a water-cooled copper mold is continuously drawn from the lower end side of the mold to obtain a slab-shaped slab having a predetermined length.
  • DC slab the slab obtained by this DC slab casting method
  • the slab obtained by this DC slab casting method usually has severe surface irregularities and many defects. If such a slab is subjected to hot rolling as it is, the surface properties of the hot rolled plate (hot rolled plate) will deteriorate. For this reason, before hot rolling, it is the actual condition that the surface must be cut by several mm to 20 mm. Therefore, the yield of the material is reduced, and the labor and cost of the cutting work are required, so there is still a strong demand for improvement.
  • the surface properties of the hot-rolled sheet after hot rolling are not necessarily good. That is, there is a problem in that many large and small cover-like wrinkles extending from a few mm to a length of about 10 mm are generated on the surface of the hot rolled sheet.
  • Such surface defects of the hot-rolled sheet are derived from the coarse cast structure of the cast slab. That is, the material for hot rolling that has not undergone the breakdown process, which is hot working, has a cast structure composed of coarse crystal grains as cast (as cast). Even if the cutting process is performed, a coarse structure exists in the surface layer after the cutting, and surface flaws are generated in the hot-rolled sheet due to such a coarse surface casting structure.
  • the surface layer of the titanium material for hot rolling obtained without undergoing the breakdown process is modified.
  • a method of applying quality treatment has already been proposed.
  • Patent Document 1 high energy is applied to the surface of the titanium slab, particularly the surface that becomes the rolling surface during hot rolling, by high frequency induction heating, arc heating, plasma arc heating, electron beam heating, or laser heating.
  • a method has been proposed in which only the surface layer is melted over a depth of 1 mm or more and immediately cooled and re-solidified.
  • the surface layer of the titanium slab is melted so that the surface is smoothed, and defects such as blow holes in the surface layer disappear, as well as heat removal from the base material side.
  • the molten layer is rapidly cooled and solidified, and at the same time the lower heat-affected layer (HAZ layer) is rapidly cooled, so that the molten layer and the HAZ layer have a fine transformation structure.
  • the surface layer thus refined is recrystallized at the time of subsequent slab heating before hot rolling, and becomes a granular structure (equiaxial grain structure) having a fine and irregular orientation. Therefore, it is possible to prevent the occurrence of dents due to the coarse structure, and it is possible to eliminate the surface flaws of the hot-rolled sheet after hot rolling.
  • a method for modifying the surface layer of the titanium slab by applying high energy to the surface of the titanium slab to melt only the surface layer and immediately rapidly solidifying it is referred to as surface melting treatment in this specification. It is called.
  • a layer obtained by melting the surface layer by the surface melting treatment and further resolidifying the molten layer is referred to as a remelted solidified layer in this specification.
  • the material for hot rolling (slab) after the surface melting treatment is referred to as a hot rolling material in this specification.
  • a hot rolled material obtained by subjecting a DC slab to surface melting treatment and then hot rolling is generally subjected to cold rolling to obtain a thickness corresponding to the product application. is there.
  • cold forming such as bending, drawing, and overhanging may be performed.
  • cracks may occur on the surface in cold rolling or cold forming after hot rolling.
  • the surface layer of the DC slab contains oxygen at a considerably high concentration (for example, an oxygen concentration having an average oxygen concentration from the surface to a depth of 0.5 mm is about 0.3 to 0.5 mass% higher than the base material). It has been found that there may be a layer (hereinafter referred to as an oxygen-contaminated layer). There are several possible causes for the oxygen contamination layer on the surface of the slab. One of them is air that enters from the outside when the chamber is opened in order to remove the cast slab from the drawing chamber after casting. May be absorbed by the slab surface.
  • the degree of vacuum in the chamber during casting in particular, the degree of vacuum around the hot slab drawn from the mold is not sufficiently high, or residual oxygen-containing gas in an inert gas atmosphere
  • the concentration may be high, and in that case, it is considered that oxygen may be absorbed by the slab surface from the atmosphere around the slab.
  • the state in which the oxygen concentration is high becomes the depth of the remelted solidified layer by the surface melting treatment. If it is deeply spread in the whole direction and further heated as a raw material for hot rolling, the oxygen concentration in the remelted solidified layer may be increased, but it will not be lowered. A deep oxygen-contaminated layer (a remelted and solidified layer having a high oxygen concentration) remains on the plate. Such a deep oxygen-contaminated layer cannot be sufficiently removed even by pickling before cold rolling, and remains in a region near the surface (remelted solidified layer if it is subjected to cold rolling or cold forming). ) And the internal region, it is considered that cracking is likely to occur due to the difference in cold workability derived from the difference in oxygen concentration.
  • the oxygen concentration of the surface layer has a gradient (oxygen concentration gradient) that increases from the inside toward the surface.
  • the oxygen concentration in the re-melted and solidified layer is averaged and the concentration gradient disappears. It is observed that the oxygen concentration becomes almost constant.
  • the average oxygen concentration in this state is the oxygen in the non-contaminated area (the area of the original slab that has not been melted and resolidified) inside the remelted and solidified layer (oxygen-contaminated layer). It is definitely higher than the concentration. This means that the oxygen concentration is stepped in the surface layer (remelted solidified layer; oxygen-contaminated layer) in the slab (material for hot rolling) after the surface melting treatment and in the vicinity of the inner region and the boundary. Means a sudden change.
  • surface melting treatment for hot rolling material is extremely effective for smoothing the surface and eliminating surface layer defects (such as blowholes), but the surface layer is contaminated with oxygen. If there is, the oxygen concentration in the contaminated layer is averaged (the oxygen concentration is uniform from the inside to the surface) and the oxygen contaminated layer is deepened (the region with a high oxygen concentration expands in the depth direction). It is thought that this causes the problem of cracking during cold rolling or cold forming as described above.
  • the surface layer of the as-cast slab is usually a layer with severe irregularities and many defects. It has been conventionally considered that the surface layer of the slab is removed by cutting over a depth of about several mm and then the surface melting treatment as described above is performed.
  • the cutting in this case is mainly aimed at removing surface irregularities and defects, but following the technique, it is also possible to remove the oxygen-contaminated layer on the surface of the DC slab by cutting and then subject it to surface melting treatment. It is done. If the surface layer (oxygen-contaminated layer) is removed prior to the surface melting process by cutting in this way, cracking occurs during cold working or cold forming due to oxygen contamination during DC casting as described above. It is possible to avoid this problem.
  • the present invention does not perform the cutting process before the surface melting process, or at least when the cutting depth of the cutting process before the surface melting process is reduced,
  • the hot forming providing a titanium slab for surface melting treatment that can reliably and stably prevent cracks on the surface, and a titanium material for hot rolling that has been subjected to surface melting treatment using the slab, As a result, it is an object to improve the productivity of titanium hot-rolled sheet manufacturing and to reduce costs.
  • the present inventors have conducted extensive experimental studies, and as a result, at the stage of the titanium slab before the surface melting treatment, the oxygen concentration gradient in the slab thickness direction of the surface layer is appropriately reduced. As a result, the inventors have found that the above-described problems can be solved, and have reached the present invention.
  • a remelted solidified layer having a depth d 1 is formed on the surface of the titanium slab by surface melting treatment, and the surface is rolled.
  • a titanium slab for surface melting treatment used when producing a titanium material by hot rolling as a surface The titanium slab is an as-cast titanium slab obtained by a DC slab casting method in a vacuum or an inert gas atmosphere, In the thickness direction of the titanium slab, A region from the surface to the position of d 1/2 is a first region, A region from the position of the d 1/2 to the position of the d 1 and the second region,
  • the increment of the average oxygen concentration in the first region and C 1, The increment of the average oxygen concentration in the second region and C 2,
  • C 1 -C 2 and C 1 and C 2 and C d C 1 : 0.20 mass% or less
  • C d: is more than 0
  • the titanium slab for surface melting treatment of the second aspect of the present invention is the titanium slab for surface melting treatment of the first aspect, wherein C d is what is not more than 0.10 mass%.
  • the titanium slab for surface melting treatment of the third aspect of the present invention is the titanium slab for surface melting treatment of the first or second aspect,
  • the d 1 is in the range of 3.0 to 10.0 mm.
  • the titanium slab for surface melting treatment of the fourth aspect of the present invention is the titanium slab for surface melting treatment of any one of the first to third aspects, The surface is cut and removed with a thickness of 3.0 mm or less.
  • the following fifth to seventh embodiments are for hot rolling, in which the surface of the above-described titanium slab for surface melting treatment is subjected to melting-rapid resolidification processing (surface melting processing) by high-density energy. This is specified for titanium materials.
  • a remelted solidified layer having a depth d 1 is formed on the surface of the titanium slab according to any one of the first to fourth aspects by surface melting treatment.
  • the titanium raw material for hot rolling according to the sixth aspect of the present invention is the titanium raw material for hot rolling according to the fifth aspect, wherein the oxygen concentration distribution in the thickness direction is a boundary between the remelted solidified layer and the base material. In the position, it increases in steps from the base material toward the surface.
  • the titanium material for hot rolling according to the seventh aspect of the present invention is the titanium material for hot rolling according to any of the fifth and sixth aspects,
  • the increment of the average oxygen concentration of the remelted solidified layer with respect to the average oxygen concentration of the base material is 0.1 mass% or less.
  • a remelted solidified layer is formed on the surface of the titanium slab by surface melting treatment, and hot rolling is performed by hot rolling using the surface as a rolling surface.
  • hot rolling is performed by hot rolling using the surface as a rolling surface.
  • FIG. 5 is an enlarged schematic view showing an IV portion of FIG. 4 as an example of an oxygen concentration distribution in a thickness direction at a cross-sectional position in an as-cast titanium slab.
  • FIG. 5A It is a schematic diagram which shows the comparative example of the oxygen concentration distribution of the thickness direction in the cross-sectional position in the as-cast titanium slab on the same scale as FIG. 5A. It is a schematic diagram which shows the comparative example of oxygen concentration distribution after performing the surface melting process with respect to a titanium slab on the same scale as FIG. 6A.
  • An example of the oxygen concentration distribution in the thickness direction at the cross-sectional position in the titanium slab according to the present invention and the concentration distribution after the surface melting treatment are as follows: It is a schematic diagram shown in contrast.
  • the method for producing the titanium slab for surface melting treatment that is, the titanium melting raw material is vacuum or non-reacted using a high-density energy heat source such as an electron beam or plasma.
  • a high-density energy heat source such as an electron beam or plasma.
  • a water-cooled copper hearth 2 disposed in a melting chamber 1 is mixed with an industrial pure titanium melting raw material, for example, a titanium sponge obtained by a crawl method, or pure titanium scrap.
  • an industrial pure titanium melting raw material for example, a titanium sponge obtained by a crawl method, or pure titanium scrap.
  • the electron beam 3 is irradiated by the electron beam irradiation gun 12 to melt the melting raw material in the hearth 2.
  • the obtained titanium melt 4 is made into a water-cooled copper mold 6 for DC slab casting disposed in the upper part of the casting-drawing chamber 5, that is, the upper and lower sides are open and the horizontal section is rectangular (chamber at the corner).
  • the water is continuously poured into the water-cooled copper mold 6.
  • the electron beam 7 is generally irradiated to the surface of the molten titanium 4 in the mold 6 separately from the melting electron beam 3. is there.
  • the hearth 2 for melting the melting raw material may be plural or multistage.
  • Titanium solidified in the mold 6 is continuously drawn downward by lowering a drawing member (liftable receiving member) 8 disposed below in the casting-drawing chamber 5.
  • a titanium slab 10 having a rectangular shape (including a case where chamfers are formed at corners) and having a predetermined length is obtained in an extraction chamber 5B described below.
  • the casting-drawing chamber 5 has a structure in which a casting chamber 5A that surrounds the mold 6 and a drawing chamber 5B below the mold 5 are vertically connected, and the lower drawing chamber 5B has a predetermined length of casting.
  • the lower drawing chamber 5B has a predetermined length of casting.
  • it is configured to move away from the upper casting chamber 5A and move to one side (for example, the left side in FIG. 1) from the original position (position at the time of casting) together with the drawing member 6.
  • a variable partition plate (valve plate) (not shown) is inserted between the casting chamber 5A and the drawing chamber 5B in order to maintain the vacuum state of the casting chamber 5A, or a variable partition plate (valve) It is common to install a short gate chamber containing a plate.
  • another extraction chamber (a chamber provided with another extraction member) is disposed on the other side (for example, the right side of FIG. 1) of the position (original position) of the extraction chamber 5B at the time of casting.
  • another extraction chamber a chamber provided with another extraction member.
  • the other drawing chamber moves below the casting chamber 5A as the original drawing chamber 5B moves to one side (for example, the left side in FIG. 1). Composed to come to the side.
  • variable partition plate when the variable partition plate (valve plate) is open, the space in the melting chamber 1 and the space in the casting-drawing chamber 5 communicate with each other by a gap around the mold 6.
  • a vacuum pump 9 is connected to the upper part of the melting chamber 1 through an exhaust pipe 9a, and the space in the melting chamber 1 and the space in the casting-drawing chamber 5 are evacuated. . Therefore, melting and casting of titanium is basically performed under vacuum exhaust. However, in practice, a very small amount of diluted inert gas may be introduced.
  • the variable partition plate is inserted.
  • the lower drawing chamber 5B moves away from the upper casting chamber 5A together with the titanium slab 10 and the drawing member 6, for example, to the left in FIG. 1, and one lot of melting / casting is completed.
  • the evacuation in the drawing chamber 5B is interrupted, and further lowered to an appropriate temperature and then released to atmospheric pressure. It will be.
  • the wide 2 of the four surfaces 10A to 10D along the length direction LD (the slab drawing direction in the DC slab casting) LD.
  • the surfaces 10A and 10B (surfaces including the chamfer 11) serve as rolling surfaces during hot rolling. Therefore, surface melting treatment is performed on the wide two surfaces 10A and 10B including at least the chamfer 11.
  • the wide two surfaces 10A The explanation will be made on the assumption that surface melting treatment is performed for 10B.
  • an electron beam is irradiated onto the surface of the wide one surface 10A of the outer surface of the titanium slab 10 by the electron beam irradiation gun 13, and only the surface layer on the surface 10A is rapidly melted.
  • the electron beam irradiation gun 13 is continuously moved or the rectangular cast piece 10 is continuously moved along the longitudinal direction LD (or short direction) of the titanium slab 10.
  • the melting position is moved to.
  • the molten layer on the surface of the titanium slab 10 at that time is denoted by reference numeral 16a in FIG.
  • the molten layer 16a in the irradiated portion has a base material (titanium slab as shown in FIG. 3). 10 is cooled by heat removal from the inside), and when it reaches a solidification temperature or lower, it solidifies and becomes a remelted solidified layer 20. In addition, due to the heat effect of the surface melting treatment, a heat affected zone (HAZ) 18 heated to a temperature equal to or higher than the ⁇ transformation point temperature (about 900 ° C.) is generated. Thereafter, the heat affected layer 22 is formed by being cooled by heat removal from the base material (inside the titanium slab 10) and reaching the ⁇ transformation point temperature or lower.
  • HZ heat affected zone
  • the remelted solidified layer 20 and the heat-affected layer 22 are collectively referred to as a surface melt-treated layer 21.
  • the melting-re-solidification process surface melting process
  • the above-described process is performed on the other surface 10B of the titanium slab 10.
  • the same processing is performed. Further, if necessary, the same processing is performed on the other surfaces 10C and 10D of the titanium slab 10.
  • the melting depth by the surface melting treatment as described above, and therefore the depth d 1 of the remelted solidified layer 20 is usually in the range of 3 mm to 10 mm.
  • the melting depth by electron beam irradiation primarily because the amount of heat input is concerned, so that the heat input, such as melt depth d 1 of the above can be obtained, selecting the electron beam irradiation conditions.
  • the amount of heat input required varies depending on the slab thickness (heat capacity), slab base material temperature, cooling conditions on the slab base material side, etc. Although not determined, normally, the heat input per unit area (per 1 cm 2 ) is about 80 to 300 J.
  • the electron beam irradiation conditions that affect the amount of heat input per unit area include the output and beam diameter of the irradiation gun, and the gun movement speed when irradiating while moving the irradiation gun continuously as described above ( (Irradiation position moving speed) and the like, and these are appropriately set to secure the above heat input.
  • the titanium slab subjected to the surface melting treatment as described above is heated as a hot rolling material to a temperature higher than the hot rolling start temperature by an appropriate heating furnace, and then the hot rolling material is hot rolled.
  • a hot-rolled sheet having a required thickness is obtained.
  • the hot-rolled sheet is subjected to descaling treatment such as pickling, and then cold-rolled to reduce the thickness to the product sheet thickness and then annealed.
  • it is subjected to cold forming as necessary and used for various purposes.
  • the titanium slab (as cast DC slab) 10 obtained by melting and casting has a cross section in the thickness direction as shown in FIG.
  • an oxygen-contaminated layer 10P containing oxygen at a high concentration for example, about 0.1 mass% or more higher than the oxygen concentration in the inner region), and in some cases at a high concentration of about 0.3-0.5 mass% or more.
  • the oxygen in the oxygen-contaminated layer 10P is mainly due to oxygen from the atmosphere outside the slab, and is caused by absorption and inward diffusion of the oxygen-containing gas. It has a gradient (oxygen concentration gradient) that decreases from the slab surface toward the inside.
  • the oxygen contamination layer 10P 0.05 mass% or more regions oxygen concentration than the base metal, the oxygen gradient slab thickness direction in FIG. 4, for example, than the average oxygen concentration C 0 of the base material 0
  • the space in the melting chamber 1 and the casting-drawing chamber 5 is originally maintained in vacuum during the melting / casting and the subsequent cooling period.
  • oxygen contamination of the titanium slab should not occur.
  • the oxygen-contaminated layer 10P is often generated.
  • a vacuum pump 9 for exhausting the inside of the chamber is generally provided on the side of the melting chamber 1 to prevent oxygen absorption during melting of the melting raw material.
  • the degree of vacuum in the space in the casting-drawing chamber 5, especially the space in the drawing chamber 5B may not be sufficiently high. Therefore, it is considered that the oxygen-containing residual gas may be absorbed by the high-temperature titanium slab 10 in the extraction chamber 5B.
  • oxygen or oxygen-containing gas that has entered from the outside when the chamber is opened is adsorbed or adhered to the inner wall of the casting-drawing chamber 5 or the outer surface of the mold 6 and is not sufficiently exhausted or evacuated. Absorption on the surface of the hot slab is considered to be one cause. In any case, it is considered that the concentration of oxygen or oxygen-containing gas in the atmosphere in the chamber becomes unexpectedly high, and an oxygen-contaminated layer is generated on the slab surface.
  • the slab in which the oxygen-contaminated layer is formed on the surface in this way is subjected to the surface melting treatment without performing surface cutting (and thus without removing the oxygen-contaminated layer), and the slab after the surface melting treatment (hot rolling) Material) is heated and hot-rolled into a hot-rolled sheet, and further cold-rolled into a cold-rolled plate or cold-rolled annealed sheet, as described above, during cold rolling or cold forming
  • the problem of cracking will occur. That is, the state in which the oxygen concentration of the surface layer in the slab is high (the state in which the oxygen-contaminated layer exists) remains after the surface melting treatment, and further heating it as a hot rolling material increases the oxygen concentration of the surface layer.
  • FIG. 5A shows a part of the oxygen concentration distribution in the slab thickness direction in the as-cast titanium slab (original material) 10 shown in FIG. 4, that is, the oxygen concentration in the vicinity of the surface 10A (circled portion IV in FIG. 4).
  • the distribution is shown enlarged.
  • FIG. 5B shows the oxygen concentration distribution of the slab after the surface melting treatment is performed on the as-cast titanium slab having the oxygen concentration distribution shown in FIG. 5A by a solid line.
  • the broken line in FIG. 5B indicates the oxygen concentration distribution of the as-cast titanium slab shown by the solid line in FIG. 5A, that is, the oxygen concentration distribution before the surface melting treatment.
  • 5C shows the oxygen concentration distribution of the hot-rolled sheet after hot rolling the slab after the surface melting treatment having the oxygen concentration distribution shown by the solid line in FIG. 5B.
  • FIG. 5D shows the oxygen concentration distribution after the hot-rolled sheet having the oxygen concentration distribution shown in FIG. 5C is pickled.
  • the oxygen concentration of the as-cast slab (base material) increases from the inside (base material side inside the base material) toward the slab surface in the surface layer.
  • the maximum value C max 1 of the oxygen concentration on the surface may reach 0.5% or more.
  • FIG. 5B shows a state after subjecting such an as-cast titanium slab to surface melting treatment.
  • the oxygen concentration distribution changes significantly when the surface melting treatment is performed (FIG. 5B) from the as-cast state (FIG. 5A). That is, in the surface melting treatment, the surface layer is melted by irradiation with an electron beam having a high density energy, and the molten metal in the molten pool is forcibly stirred by the energy, so that oxygen is stirred and flowed in the molten pool, As a result, the oxygen concentration gradient in the molten layer is averaged, and as a result, the oxygen concentration gradient before the surface melting treatment substantially disappears, and in the remelted solidified layer (region from the surface to the depth d 1 ) 20 after melting, The oxygen concentration is almost uniform.
  • the oxygen concentration of the remelted solidified layer 20 is high in a stepped manner with respect to the substantially uniform oxygen concentration C 0 (usually about 0.04 to 0.2 mass%) in the inner region (base material) free from oxygen contamination. It becomes the state (oxygen concentration C m ). That is, in the slab (hot rolling material) after the surface melting treatment, the vicinity of the boundary between the surface layer (remelted solidified layer 20) and the inner side region (strictly speaking, in the surface melting treatment layer) In the vicinity of the boundary between the remelted solidified layer 20 and the heat-affected layer 22), the oxygen concentration changes steeply in steps.
  • the value C m of the oxygen concentration of the remelted solidified layer 20 after the surface melting is almost the entire region in the thickness direction before the treatment. Although it becomes smaller than the maximum value C max 1 of the surface, it will surely become higher than the average oxygen concentration C 0 in the inner region without oxygen contamination.
  • the surface melting treatment the oxygen concentration than the average oxygen concentration C 0 of the absence of oxygen contamination inner region is high region (region of the oxygen concentration C m) is, the inner side of the plate It means to greatly expand.
  • the increment of the oxygen concentration C m remelting solidified layer 20 relative to the average oxygen concentration C 0 of the internal region (base material portion), a ⁇ C m ( C m -C 0 ).
  • the slab after the surface melting treatment is heated and subjected to hot rolling as a material for hot rolling.
  • FIG. 5C shows the oxygen concentration at the very thin layer portion on the surface of the hot-rolled plate.
  • C max 2 for example, an oxide having an oxygen concentration of about 35% or more
  • very thin surface generally a thickness d 3 is a layer of about 0.03 ⁇ 0.1 mm
  • thick layer d 3 is common to dissolve and remove the This usually removes the oxygen-enriched layer on the surface generated by heating-hot rolling.
  • FIG. 5D shows the oxygen concentration distribution after the pickling.
  • the depth may be larger or smaller than the depth up to P q , in practice, it is desirable to make the oxygen concentration larger than the depth from the slab surface to the position P q of C q .
  • the surface melting treatment as described above is derived from the existence of the oxygen contamination layer on the surface of the titanium slab and the change in the oxygen concentration distribution of the surface layer when the surface melting treatment is applied to the slab.
  • cracks are considered to occur during cold rolling or cold forming after cold-rolled sheet annealing.
  • a remelted solidified layer having a depth d 1 is formed on the surface of the titanium slab by surface melting treatment, and hot rolling with the surface as a rolling surface is performed.
  • a region from the surface to a position of d 1/2 in the thickness direction of the titanium slab is defined as a first region, and from the position of d 1/2
  • the region up to the position of d 1 is a second region, and the average oxygen concentration increment in the first region is C 1 with respect to the average oxygen concentration of the base material of the titanium slab, and the average oxygen in the second region is the increment of the concentration of C 2, when the difference C 1 -C 2 and C 1 and C 2 and C d, C 1: 0.20 mass% or less, C 2: 0.05 mass% or less, and C d: 0 over 0 If it is 15 mass% or less, the difference in oxygen concentration between the remelted solidified layer after the surface melting treatment and
  • the oxygen contamination layer having a high oxygen concentration is generated, the oxygen concentration gradient of the surface layer is also increased, and the slab (comparative slab) when the above conditions are not satisfied is the thickness before the surface melting treatment.
  • the directional oxygen concentration distribution is shown in FIG. 6A on the same scale as the thickness direction oxygen concentration distribution in the stage before the surface melting treatment in the slab of the present invention shown in FIG. 5A.
  • the thickness direction oxygen concentration distribution after performing the surface melting treatment is the same as the thickness direction oxygen concentration distribution in the stage before the surface melting treatment in the slab of the present invention shown in FIG. Shown in
  • the average oxygen concentration in the region inside the oxygen-contaminated layer is not substantially affected by oxygen absorption from the surface. Accordingly, the oxygen amount in the region inside the slab is not different between the comparison slab and the slab of the present invention, and can be regarded as the same. Therefore, in FIGS. 6A and 6B for the comparison slab, FIG. as with FIG. 5B, the average oxygen concentration inside are shown as the same value C 0.
  • a slab (comparative slab; FIGS. 6A and 6B) when the oxygen contamination layer having a high oxygen concentration is generated as described above, the oxygen concentration gradient of the surface layer is increased, and the above condition is not satisfied.
  • the slab that satisfies the above conditions the slab of the present invention; FIGS. 5A and 5B
  • the oxygen concentration distribution in the thickness direction before the surface melting treatment, and the slab (the material for hot rolling) after the surface melting treatment The oxygen concentration distribution in the thickness direction is shown in the same FIG.
  • Comparative slab as shown in FIG. 6A, the region (first region from the slab surface to a position of 1/2 of the depth d 1 of the re-melting and solidification layers 20 in the slab thickness direction (i.e. d 1/2) ) of the average oxygen concentration of the R1, regions of the incremental C 1 'from the base material average oxygen concentration C 0, to a position corresponding to a depth d 1 remelting solidified layer from the position of d 1/2 in the slab thickness direction (Second region)
  • the oxygen concentration distribution in the thickness direction before the surface melting treatment is indicated by a two-dot chain line in FIG.
  • the maximum oxygen concentration (oxygen concentration at the surface position) of the surface layer (oxygen-contaminated layer) is indicated by C max 1 ′.
  • the oxygen concentration distribution in the slab thickness direction after the surface melting treatment is performed from the surface at a depth d (the depth of the remelted solidified layer is d 1 ) is shown by a dotted line in FIG.
  • the oxygen concentration in the thickness direction is averaged, and the oxygen concentration of C m ′ is almost uniform. That is, the oxygen concentration in the thickness direction has a distribution that increases stepwise at the boundary position between the remelted solidified layer and the base material. In the vicinity of the position of the depth d 1 (the boundary position between the remelted solidified layer 20 and the base material), the oxygen concentration is rapidly and greatly changed from C 0 to C m ′ in the thickness direction. .
  • the present invention slab, the average oxygen concentration in the first region R1, and the incremental C 1 against the base material average oxygen concentration C 0, the average oxygen concentration in the second region R2, increment for the base material average oxygen concentration C 0 C the difference C d and 2 is of the following 0.15 mass%.
  • the oxygen concentration distribution in the thickness direction before the surface melting treatment is shown by broken lines in FIG.
  • the maximum oxygen concentration (oxygen concentration at the surface position) of the surface layer (oxygen-contaminated layer) is indicated by C max 1.
  • the first region R1 of the average oxygen concentration in the second region R2 if the difference between C d increment from the base material average oxygen concentration C 0 of 0.15 mass% satisfy the following conditions present invention slabs ( That is, C d ⁇ 0.15 mass%) does not satisfy the condition that the difference C d of the average oxygen concentration in the first region R1 and the second region R2 from the base material oxygen concentration C 0 is 0.15 mass% or less.
  • the oxygen concentration gradient (gradient) in the thickness direction is smaller than that of the comparative slab (that is, C d ′> 0.15 mass% in the comparative slab).
  • the average oxygen concentration in the non-oxygen-contaminated region inside the slab is the same C 0 , the smaller the oxygen concentration gradient (slope) in the thickness direction, the smaller the oxygen concentration (maximum oxygen concentration) at the surface position.
  • the maximum oxygen concentration) C max 1 is lower than the oxygen concentration (maximum oxygen concentration) C max 1 ′ at the surface position in the comparative slab.
  • the total amount of oxygen contained from the surface to the position of the depth d 1 is also smaller in the slab of the present invention than in the comparative slab.
  • the oxygen concentration distribution in the slab thickness direction is shown.
  • the slab as the tendency of the oxygen concentration distribution in the thickness direction after a surface melting treatment, similar to the oxygen concentration distribution in the thickness direction after the surface melting treatment of the comparative slabs, re-melting and solidification of the depth d 1 the layers within 20, is the oxygen concentration averaged in the thickness direction, are approximately constant in the thickness direction increment [Delta] C m of substantially constant oxygen concentration C m becomes, the preform oxygen concentration C 0.
  • the oxygen concentration distribution in the thickness direction is a step-like distribution.
  • a substantially constant oxygen concentration C m the position of the depth d 1 from the vicinity of the surface in comparison slab after the surface melting treatment (broken line in FIG. 7) to close the position of the depth d 1 from the vicinity of the surface in the present invention the slab It becomes smaller than the almost constant oxygen concentration C m ′ up to near. This is because, as described above, the total amount of oxygen contained from the surface to the position of the depth d 1 is smaller in the slab of the present invention than in the comparative slab.
  • the oxygen concentration changes from C 0 to C m in a stepped manner in the thickness direction.
  • oxygen concentration difference C d is more than 0.15 mass%, the boundary between the re-melting and solidification layer and it than the inner region after the surface melting treatment
  • the change in oxygen concentration in the vicinity increases (for example, the increment ⁇ C m of the oxygen concentration C m of the remelted solidified layer from the base material average oxygen concentration C 0 exceeds 0.1% after the surface melting treatment) .
  • increment C 1 from the base material of oxygen concentration C 0 of the first region R1 is higher than 0.2 mass%, or increments C 2 from the base material of oxygen concentration C 0 of the second region R2 is zero. Even in the case where it exceeds 05%, the change in oxygen concentration near the boundary between the remelted solidified layer and the inner region after the surface melting treatment becomes large (for example, the base material oxygen concentration in the state after the surface melting treatment).
  • the increment ⁇ C m of the oxygen concentration C m of the remelted solidified layer from C 0 exceeds 0.1%). As a result, it becomes difficult to prevent the occurrence of cracking during cold rolling of the hot-rolled sheet as described above and crack peeling during cold forming of the cold-rolled annealed sheet.
  • the depth (depth from the surface position of the base plate before the treatment) d 1 of the remelted solidified layer in the surface melting treatment applied to the slab a range of 3.0 to 10.0 mm It is preferable to be inside. If the depth of the remelted solidified layer is less than 3.0 mm, the effect of smoothing the surface layer and removing defects in the surface layer by performing the surface melting treatment cannot be obtained sufficiently. On the other hand, even if the thickness exceeds 10.0 mm, the effect of the surface melting treatment does not increase any more, and unnecessarily increases the energy cost and decreases the productivity.
  • the depth of the first region and the second region as a reference for the thickness direction concentration gradient of the surface layer of the slab is determined to be 1 ⁇ 2 of the depth d 1 of the surface melting treatment to be performed thereafter. and which, therefore, specific depths of the regions (d 1/2) is about 0.15 ⁇ 5 mm.
  • the maximum oxygen concentration at the surface position is usually reduced as described above. Even without cutting, it is possible to obtain the actions and effects as described above. However, in some cases, it is allowed to perform surface melting treatment after removing a very thin layer on the surface by cutting. However, the cutting depth in that case is a depth smaller than 3.0 mm.
  • the concentration gradient in the depth direction of oxygen does not change, but since the high oxygen concentration portion has been removed by cutting, the total of the remelted solidified layer
  • the oxygen amount of the first region R1 and the second region R2 is reduced, and the difference C d between the increments C 1 and C 2 from the base material oxygen concentration C 0 in each region is reduced.
  • the above difference C d can be obtained 0.15 mass% or less of the slab.
  • the cutting depth of the surface layer exceeds 3.0 mm, the burden of cutting processing increases, and the productivity may be hindered. Therefore, when cutting, the depth is set to 3.0 mm or less.
  • Countermeasure A is a technique for mainly preventing oxygen contamination when the atmosphere is released after completion of melting and casting.
  • Countermeasure B and Countermeasure C are methods mainly for preventing oxygen contamination during melting and casting. In practice, it is preferable to apply a combination of two or more of these.
  • Measure A Oxygen absorption of the slab due to the intrusion of the atmosphere into the chamber when the atmosphere is open is likely to occur when the slab is still at a high temperature. Prone to occur in some cases. Therefore, after melting and casting a slab having a predetermined length, the air is released to the atmosphere after the surface temperature of the slab becomes about 900 ° C. or less. At this time, it may be left in the chamber, or accelerated cooling may be performed to improve productivity.
  • a cooling means for cooling the slab may be provided in the drawing chamber, and the air may be opened to the atmosphere in a state where the surface temperature is about 900 ° C. or lower.
  • the cooling means for example, it is possible to apply a cooling plate whose inside is cooled with water in a state of being close to the slab.
  • a low-temperature gas such as an inert gas before the atmosphere is released
  • the surface temperature is quickly reduced to about 900 ° C. or lower, and the slab surface becomes a low temperature of 900 ° C. or lower. It is good also as opening in the atmosphere.
  • the vacuum pump 9 (see FIG. 1) for evacuating the chamber is generally evacuated at a location away from the casting-drawing chamber 5 mainly for the purpose of keeping the melting chamber 1 in a vacuum.
  • a second vacuum pump 91 is provided separately from the vacuum pump 9 for evacuation of the melting chamber, for example, as shown by a chain line in FIG.
  • the exhaust pipe 91a of the second vacuum pump 91 is connected to the side of the drawing chamber 5B that is opened to increase the degree of vacuum in the casting / drawing chamber 5 during melting / casting.
  • Countermeasure C In order to lower the partial pressure of oxygen and oxygen-containing gas in the atmosphere during melting and casting, for example, as shown by the chain line in FIG. A member 92 made of a high target material such as titanium or zirconium is provided. In addition, in order to increase the degree of vacuum in the chamber during casting and melting, a vacuum pump having a larger exhaust capacity may be used. Moreover, you may use together means, such as improving the airtightness in the chamber at the time of casting and melt
  • the industrial pure titanium constituting the titanium slab of the present invention includes 1 to 4 types of JIS standards, Grades 1 to 4 of ASTM standards corresponding thereto, and DIN standards 3, 7025, 3, 7025, 3.
  • Industrial pure titanium specified in 7025 shall be included. That is, the industrial pure titanium targeted in the present invention is, in mass%, C: 0.1% or less, H: 0.015% or less, O: 0.4% or less, N: 0.07% or less, It can be said that Fe: 0.5% or less and the balance Ti. Furthermore, a small amount of platinum group elements are added to these, and a high corrosion resistance alloy (ASTM Grade 7, 11, 16, 26, 13, 30, 33) called modified (improved) pure titanium or JIS corresponding to these. In the present invention, the seed is also treated as being contained in industrial pure titanium.
  • the size of the surface treatment titanium slab 10 of the present invention is not particularly limited as long as it can be directly subjected to hot rolling, but coil rolling is applied as hot rolling, and a hot rolled coil having a thickness of about 3 mm to 8 mm.
  • the titanium slab may have a thickness of about 150 mm to 280 mm, a length of about 3 m to 10 m, and a width of about 600 mm to 1500 mm.
  • hot rolling is performed to obtain a hot rolled sheet having a desired thickness.
  • the hot rolling method is not particularly limited, but in the case of a thin hot-rolled sheet product, coil rolling is usually applied.
  • the thickness of the hot rolled sheet is not particularly limited, but is usually about 3.0 mm to 8.0 mm.
  • the hot rolling conditions are not particularly limited, as in normal titanium hot rolling, heating is performed from 720 ° C. to 920 ° C. for about 60 minutes to 420 minutes, and hot rolling is started at a temperature within the range, What is necessary is just to complete
  • Test Example 1 Using JIS type 1 pure titanium as a melting raw material, DC casting was performed by electron beam melting using equipment as shown in FIG. 1 to obtain a titanium slab having a cross section of about 1300 mm wide ⁇ about 400 mm thick ⁇ about 7500 mm long. The casting speed was 2 ton / h.
  • any one or more of the measures A to C was applied to suppress the oxygen concentration in the surface layer of some slabs (Nos. 1 to 6 in Table 1).
  • some slabs No. 7 in Table 1
  • no measures were taken to suppress the oxygen concentration in the surface layer.
  • surface melting treatment by electron beam irradiation was performed while continuously moving the slab on two wide surfaces of the slab to obtain a titanium material for hot rolling.
  • an electron beam adjusted to have a rectangular electron beam size of 2.5 cm is used, and other electron beam irradiation conditions (electron beam output, slab moving speed during irradiation, heat input per cm, etc.) the varied, varying d 1 (depth of remelting solidification layers) melt depth from the surface position of the slab.
  • the oxygen concentration and its distribution of the surface layer of the wide surface of each titanium slab before the surface melting treatment were quantitatively examined by EPMA analysis (X-ray microanalyzer) on the cross section. That is, the surface oxygen concentration C max and the average oxygen concentration C 0 of the base material portion are examined, and the depth (d 1 ) of the target (planned) remelted solidified layer by the surface melting treatment to be performed thereafter is defined as d 1.
  • the oxygen concentration in the region (first region R1) to / 2 the increment C 1 relative to the average oxygen concentration C 0 of the base material portion, and the depth d 1/2 to d 1 region (second region R2)
  • the increment C 2 of the oxygen concentration with respect to the average oxygen concentration C 0 of the base material portion was examined.
  • Tables 1 and 2 show the results of examining the oxygen concentration and the distribution of the surface layer for 1 to 12.
  • the surface-melted titanium material for hot rolling obtained as described above was inserted into a furnace at 800 ° C., heated for about 240 minutes, and then hot rolled to a thickness of 5 mm by a continuous hot rolling strip mill.
  • a plate coil was manufactured, passed through a continuous pickling line made of nitric hydrofluoric acid, and cut by about 40 ⁇ m per side.
  • the cold formability test was performed by the Eriksen test (based on JIS Z 2247).
  • the oxygen concentration from the surface to the position of d 1 (that is, from the surface of the remelted solidified layer to the bottom) is almost equal.
  • the increment ⁇ C m with respect to the oxygen concentration C 0 of the base material portion was constant and not more than 0.1 mass%.
  • Test Example 2 Using ASTM grade 2 pure titanium as a melting raw material, DC casting was performed by electron beam melting using equipment as shown in FIG. 1 to obtain a titanium slab having a cross section of about 1100 mm wide ⁇ about 220 mm thick ⁇ about 7000 mm long. The average casting speed was 1.9 ton / h.
  • any one or more of the measures A to C was applied to suppress the oxygen concentration in the surface layer of some slabs (Nos. 13 to 18 in Table 4). For some slabs (No. 19 in Table 4), no measures were taken to suppress the oxygen concentration in the surface layer.
  • the DC slab manufactured under the same conditions as the slab No. 19 was subjected to surface cutting (cutting depth of 0.5 to 2.5 mm) before the next surface melting treatment. 20 to 24 slabs were used.
  • surface melting treatment by electron beam irradiation was performed while continuously moving the slab on two wide surfaces of the slab to obtain a titanium material for hot rolling.
  • an electron beam adjusted to have a rectangular electron beam size of 2.5 cm is used, and other electron beam irradiation conditions (electron beam output, slab moving speed during irradiation, heat input per cm, etc.) the varied, varying d 1 (depth of remelting solidification layers) melt depth from the surface position of the slab.
  • Tables 4 and 5 show the results of examining the oxygen concentration of the surface layer and the distribution thereof for 13 to 24.
  • the surface-melted titanium material for hot rolling obtained as described above was inserted into a furnace at 800 ° C., heated for about 240 minutes, and then hot rolled to a thickness of 5 mm by a continuous hot rolling strip mill.
  • a plate coil was manufactured, passed through a continuous pickling line made of nitric hydrofluoric acid, and cut by about 40 ⁇ m per side.
  • the oxygen concentration from the surface to the position of d 1 (that is, from the surface to the bottom of the remelted solidified layer) is almost constant.
  • the increment ⁇ C m with respect to the average oxygen concentration C 0 of the base material part was 0.10 mass% or less.

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Abstract

La présente invention concerne une brame en titane destinée à un traitement de fusion de surface et utilisée lors de la production d'un matériau en titane en formant une couche refondue/solidifiée ayant une profondeur d1, par l'intermédiaire d'un traitement de fusion de surface, sur une surface d'une brame en titane dans un état brut de coulée obtenu par une coulée DC de la brame, sous vide ou dans une atmosphère de gaz inerte, puis par un laminage à chaud en utilisant la surface à titre de surface de laminage. Une augmentation C1 de la concentration d'oxygène moyenne dans une première région (une région entre la surface et une position en d1/2) est inférieure ou égale à 0,20 % en masse. Une augmentation C2 de la concentration d'oxygène moyenne dans une seconde région (une région entre la position en d1/2 et une position en d1) est inférieure ou égale à 0,05 % en masse par rapport à la concentration d'oxygène moyenne d'un matériau de base destiné à la brame en titane, dans le sens de l'épaisseur de la brame en titane. L'expression Cd (= C1 - C2) est supérieure à 0 et inférieure ou égale à 0,15 % en masse. La brame en titane pour traitement de fusion de surface présente une excellente aptitude au façonnage lors d'un laminage à froid ou d'un moulage à froid après un laminage à chaud.
PCT/JP2016/072040 2015-07-29 2016-07-27 Brame en titane pour traitement de fusion de surface et matériau en titane pour laminage à chaud utilisant ladite brame Ceased WO2017018454A1 (fr)

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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
WO2014163089A1 (fr) * 2013-04-01 2014-10-09 新日鐵住金株式会社 Brame de titane pour laminage à chaud et son procédé de fabrication

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JPS63165047A (ja) * 1986-12-25 1988-07-08 Kobe Steel Ltd 電子ビ−ムによる連続溶解・鋳造方法
AU1474692A (en) * 1991-06-05 1992-12-10 General Electric Company Method and apparatus for casting an electron beam melted metallic material in ingot form
WO2010090352A1 (fr) * 2009-02-09 2010-08-12 新日本製鐵株式会社 Matériau titane pour laminage à chaud et son procédé de fabrication
RU2566691C2 (ru) * 2011-04-22 2015-10-27 Ниппон Стил Энд Сумитомо Метал Корпорейшн Титановый сляб для применения в горячей прокатке и способ его получения

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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
WO2014163089A1 (fr) * 2013-04-01 2014-10-09 新日鐵住金株式会社 Brame de titane pour laminage à chaud et son procédé de fabrication

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