TW201718890A - Titanium composite material, and titanium material for use in hot rolling - Google Patents

Abstract

This titanium composite material 1 is provided with an inner layer 5 comprising an industrial pure titanium or titanium alloy, a surface layer 3 which is formed on at least one side of the inner layer 5 and which has a chemical composition different from that of the inner layer 5, and an intermediate layer which is formed between the inner layer 5 and surface layers 3 and which has a chemical composition different from that of the inner layer 5, wherein surface layers 3 have a thickness of no less than 2 [mu]m and make up no more than 40% of the total thickness per side, and the intermediate layer has a thickness of no less than 0.5 [mu]m. The chemical composition of the surface layer 3 is B:0.1-3.0% and the remainder being titanium and impurities. This titanium composite material has prescribed neutron blocking properties despite being inexpensive.

Description

Titanium composite and titanium for hot rolling

The present invention relates to a titanium composite material and a titanium material for hot rolling.

Titanium is excellent in properties such as corrosion resistance, oxidation resistance, fatigue resistance, hydrogen embrittlement resistance, and neutron blocking properties. These properties can be achieved by the addition of various alloying elements in the titanium.

In equipment for handling radioactive waste such as nuclear power generation related equipment, a sub-line shielding plate that shields thermal neutrons is used. The neutron masking effect is the highest in the presence of 19.9% boron 10 ( ¹⁰ B) in the natural B. Generally, stainless steel containing B or the like is used as a material for the neutron shielding sheet.

Japanese Patent Publication No. Sho 58-6704 (Patent Document 1) discloses a neutron-line shielding material which is rich in hydrated magnesium borax (2MgO.3B ₂ O ₂ .13H ₂ O) and slanted borocalcium. stone _{(Moyerhofferit, 3CaO.3B 2 O 2 .7H} 2 O), colemanite _{(2CaO.3B 2 O 2 .5H 2 O} ) , etc. borate containing water of crystallization aggregate, and hemihydrate gypsum, aluminum acid An inorganic binder such as calcium cement or the like, which is formed by kneading with water, and contains 5% by mass or more of B. However, the sub-wire shielding material disclosed in Patent Document 1 is composed of cement, and thus has problems in terms of corrosion resistance, manufacturability, and even workability.

The use of a B-containing titanium alloy which is superior in corrosion resistance to stainless steel for use in neutron wire shielding materials has also been studied by the industry. For example, Japanese Patent Publication No. Hei-1-168833 (Patent Document 2) discloses the use of a boron-containing titanium alloy containing 0.1 to 10% by mass of B and the balance being composed of titanium and unavoidable impurities. Hot rolled sheet.

Japanese Patent Publication No. 5-142392 (Patent Document 3) discloses a method of filling a hollow metal casing with a boron-containing material (NaB ₄ O ₇ , B ₂ O ₃ , PbO, Fe ₂ O _{3 ,} etc.). A radiation shielding material in a solidified state in which the flowing material and the metal oxide mixed therein are formed. According to Patent Document 3, boron and hydrogen are mainly used to block the neutron beam, and the gamma ray is blocked by the casing and the metal therein.

Titanium is generally produced by the method shown below. First, titanium oxide as a raw material is chlorinated to form titanium tetrachloride by a Kroll method, and then reduced by magnesium or sodium, whereby a sponge-like metal titanium (sponge titanium) is produced in a bulk form. This sponge titanium was press-formed to form a titanium consumable electrode, and the titanium consumable electrode was subjected to vacuum arc melting as an electrode to produce a titanium ingot. At this time, a titanium alloy ingot is produced by adding an alloying element as necessary. Then, the titanium alloy ingot is divided, forged, and rolled to form a titanium flat embryo, and then the titanium flat blank is further subjected to hot rolling, annealing, pickling, cold rolling, and vacuum heat treatment to produce a titanium thin plate.

Further, as a method for producing a titanium thin plate, a titanium ingot is divided into pieces, hydrocrushed, dehydrogenated, powder disintegrated, and classified to produce a titanium powder, and the titanium powder is produced by powder rolling, sintering, and cold rolling. Method for people Known.

Japanese Laid-Open Patent Publication No. 2011-42828 (Patent Document 4) discloses a method of producing a titanium thin plate from a titanium powder directly from a titanium ingot but directly from titanium sponge, and a titanium thin plate is produced from the obtained titanium powder. The method for producing a thin plate is to form a sintered thin plate by forming a viscous composition containing a titanium metal powder, a binder, a plasticizer, and a solvent into a thin plate-like sintered body, and compacting the sintered sheet to produce a sintered compact. The thin plate is sintered, and the sintered compacted sheet is further sintered, wherein the sintered sheet has a breaking elongation of 0.4% or more, a density ratio of 80% or more, and a density ratio of the sintered compacted board of 90% or more.

Japanese Laid-Open Patent Publication No. 2014-19945 (Patent Document 5) discloses that a titanium alloy powder made of a titanium alloy scrap or a titanium alloy ingot is appropriately added with iron powder, chromium powder or copper powder to form a composite powder. The composite powder is encapsulated and extruded as carbon steel, and the encapsulation of the surface of the obtained round rod is dissolved and removed, and then subjected to a solution treatment or a solution treatment and a aging treatment, and is produced by a powder method. A method of high quality titanium alloy.

In JP-A-2001-131609 (Patent Document 6), it has been disclosed that a titanium sponge powder is filled in a copper-clad form, and then subjected to inter-temperature extrusion processing at an extrusion ratio of 1.5 or more and an extrusion temperature of 700 ° C or lower. Further, the outer peripheral processing for removing the outer copper is performed, and 20% or more of the entire length of the grain boundary of the molded body is a metal contact titanium molded body.

When the hot-rolled material is hot-rolled, when the hot-rolled material is a so-called difficult-to-machine material having a high heat-delay resistance such as pure titanium or a titanium alloy, the roll is rolled into Thin sheet technology, Stacking rolls are known. The laminating method refers to a method in which a core material such as a titanium alloy having poor workability is coated with a coating material such as carbon steel having good workability and is hot-rolled.

Specifically, for example, a release agent is applied to the surface of the core material, and at least the upper and lower surfaces thereof are coated with the covering material, or the peripheral surfaces thereof are covered with a spacer other than the upper and lower surfaces, and the surrounding portions are welded and combined. Hot rolling. In the lamination rolling, the core material of the rolled material is coated with a covering material and then hot rolled. Therefore, the surface of the core material does not directly contact the cold medium (atmosphere or roll), and the temperature of the core material can be suppressed from being lowered, so that even a core material having poor workability can be manufactured.

In Japanese Laid-Open Patent Publication No. SHO-63-207401 (Patent Document 7), a method of combining a sealed container is disclosed. In Japanese Patent Laid-Open Publication No. Hei 09-136102 (Patent Document 8), it is disclosed that it is set to 10 ^-3 A method of producing a sealed coating box by sealing a covering material at a vacuum level of a Torr or higher is disclosed in Japanese Laid-Open Patent Publication No. Hei 11-057810 (Patent Document No. 9), which is coated with carbon steel (coated material). A method of manufacturing a sealed coated box by sealing with a high energy density welding under a vacuum of 10 ^-2 Torr or less.

On the other hand, as a method of manufacturing a material having high corrosion resistance at a low cost, a method of joining a titanium material to a surface of a material of a base material is known.

Japanese Patent Publication No. 08-141754 (Patent Document 10) discloses that a steel material is used as a base material, and titanium or a titanium alloy is used as a laminate, and the joint surface of the base material and the laminate is vacuum-exhausted. The welding combination forms a combined flat embryo for rolling, and a method for producing a titanium clad steel sheet which is joined by hot rolling.

Japanese Patent Publication No. Hei 11-170076 (Patent Document 11) discloses that a surface of a base material steel material containing 0.03% by mass or more of carbon is separated by a content of pure nickel, pure iron, and carbon of 0.01% by mass. After the titanium foil is laminated and laminated with a thickness of 20 μm or more, which is formed of any of the following low carbon steels, the laser beam is irradiated from either side of the lamination direction, and at least the edge of the titanium foil is adjacent to the edge. A method of manufacturing a titanium-coated steel material by melting and joining the base material over the entire circumference.

Japanese Laid-Open Patent Publication No. 2015-045040 (Patent Document 12) discloses a method of forming a dense titanium material (titanium ingot) which is formed into a surface of a porous titanium material (sponge titanium) which is formed into an ingot shape. A titanium ingot having a surface layer of dense titanium is produced by electron beam melting under vacuum, and hot rolled and cold rolled, and a dense titanium material (titanium ingot) is produced with very little energy; The titanium material (titanium ingot) has a porous portion in which a porous titanium material is formed into an ingot shape, and a dense coating portion which is made of dense titanium and covers all surfaces of the porous portion.

In JP-A-62-270277 (Patent Document 13), the surface effect treatment of an automobile engine member by spraying is described.

[Previous Technical Literature] [Patent Document]

[Patent Document 1] Japanese Patent Publication No. 58-6704

[Patent Document 2] Special Fair No. 1-168833

[Patent Document 3] Japanese Patent Laid-Open No. Hei 5-142392

[Patent Document 4] Japanese Patent Laid-Open Publication No. 2011-42828

[Patent Document 5] Japanese Patent Laid-Open Publication No. 2014-19945

[Patent Document 6] Japanese Laid-Open Patent Publication No. 2001-131609

[Patent Document 7] JP-A-63-207401

[Patent Document 8] Japanese Patent Laid-Open No. 09-136102

[Patent Document 9] Japanese Patent Laid-Open No. Hei 11-057810

[Patent Document 10] Japanese Patent Laid-Open Publication No. 08-141754

[Patent Document 11] Japanese Patent Laid-Open No. Hei 11-170076

[Patent Document 12] Japanese Patent Laid-Open Publication No. 2015-045040

[Patent Document 13] Japanese Laid-Open Patent Publication No. 62-270277

In the hot-rolled sheet disclosed in Patent Document 2, since the B content is high, the increase in cost is undeniable, and the workability is not good, and it is actually difficult to use it as a neutron shielding sheet.

Further, the radiation shielding material disclosed in Patent Document 3 is formed by filling a boron-containing material into a metal casing material, but processing after filling with a boron-containing material is difficult.

In the prior art, when a titanium material is produced by hot working, a sponge titanium is press-formed into a titanium consumable electrode, and the titanium consumable electrode is used as an electrode to perform vacuum arc melting to produce a titanium ingot, and then the titanium ingot is further divided. The titanium flat embryo is formed by block, forging, and rolling, and the titanium flat blank is further subjected to hot rolling, annealing, pickling, and cold rolling to complete the production.

In this case, it is necessary to add a step of melting titanium to produce a titanium ingot. Although a method of producing titanium powder by powder rolling, sintering, and cold rolling is also known, a method of producing titanium powder from a titanium ingot is required to add a step of melting titanium.

In the method for producing a titanium material from titanium powder, even if it is not used as a raw material without using a high-priced titanium powder, the obtained titanium material becomes very expensive. The methods disclosed in Patent Document 7 to Patent Document 8 are also the same.

In the lamination rolling, the core material coated with the covering material is in any case a flat embryo or an ingot, and it is not possible to reduce the manufacturing cost by a melting step or a high-priced titanium powder as a raw material.

In Patent Document 12, a dense titanium material can be produced with very little energy. However, it is required to melt the surface of the sponge titanium formed into an ingot shape, and the dense titanium surface layer portion and the inner composition are the same kind of pure titanium or titanium. In the alloy, for example, the titanium alloy layer is formed uniformly and over a wide range only in the surface layer portion, and the manufacturing cost cannot be reduced.

On the other hand, a material made of titanium or a titanium alloy is bonded to the surface of the base material at an inexpensive corrosion-resistant material, and most of the base material is steel. Therefore, if the titanium layer on the surface is lost, the corrosion resistance is impaired. It is assumed that the base material is also made of titanium, and as long as the titanium material produced by the general manufacturing steps is used, a fundamental cost improvement cannot be expected. Therefore, the present inventors have considered that the surface layer of the flat embryo composed of industrial pure titanium or titanium alloy is contained. An alloy layer having a specific alloying element, and a titanium material which is inexpensive and has excellent specific properties is obtained.

As in Patent Document 13, a melting method is a method in which a metal, a ceramic, or the like is melted and sprayed onto a surface of a titanium material to form a film. When the film is formed according to this method, the formation of pores in the film is inevitable. Usually, in order to avoid oxidation of the film during the spraying, the film is sprayed while being shielded with an inert gas. These inert gases are drawn into the pores of the membrane. The pores containing such an inert gas are not pressed by heat processing or the like. Further, in the production of titanium, vacuum heat treatment is generally carried out. However, during the treatment, the inert gas in the pores expands to cause peeling of the film. According to the experience of the inventors of the present invention, the existence ratio (void ratio) of the pores generated by the spray is several vol.% or more, and the molten condition is more than 10 vol.%. As described above, the titanium material having a high void ratio in the film may be peeled off during the production step, and there may be defects such as breakage during processing.

As a method of forming the film, there is a cold spray method. According to this method, it is also the case that a film is formed on the surface, and an inert high pressure gas is used. According to this method, the void ratio can be made less than 1 vol.% depending on the conditions, but it is extremely difficult to completely prevent the occurrence of pores. Moreover, as in the case of the spray, the pores contain an inert gas, so that they are not destroyed even by subsequent processing. Further, in the case where heat treatment is applied in a vacuum, the inert gas in the pores may swell, so that the film may be broken.

In order to suppress the surface flaw during hot rolling, as a treatment for melting the surface layer of the flat embryo with an electron beam and re-solidifying, there is a melt re-solidification treatment. Usually, the surface layer that is melted and resolidified is pickled by hot rolling. Steps are removed. Therefore, in the previous melt resolidification treatment, segregation of the alloy component of the surface layer portion was not considered at all.

The present inventors have attached a titanium plate containing a specific alloying element to the surface of a flat embryo made of pure titanium or a titanium alloy for industrial use, and used the resultant as a material for hot rolling. According to the titanium material which is inexpensive and has excellent performance.

An object of the present invention is to obtain an inexpensive product by reducing the content of an alloying element added to enhance neutron blocking properties (the amount of a specific alloying element used to express a target characteristic) and suppressing the manufacturing cost of the titanium material. A titanium composite material having a desired neutron-shielding property and a titanium material for hot rolling.

The present invention has been developed to solve the above problems, and is based on the following titanium composite materials and titanium materials for hot rolling.

(1) A titanium composite material comprising: an inner layer containing industrial pure titanium or a titanium alloy; and a surface layer formed on at least one of the rolled surfaces of the inner layer, having a chemical composition different from the inner layer; And an intermediate layer formed between the inner layer and the surface layer, having a chemical composition different from the inner layer; and the surface layer has a thickness of 2 μm or more, and the ratio of the total thickness is 40 per one-sided layer. %the following; The chemical composition of the surface layer portion is, in mass%, B: 0.1 to 3.0%, and the balance: titanium and impurities; and the thickness of the intermediate layer is 0.5 μm or more.

(2) The titanium composite material according to (1) above, wherein the surface layer other than the rolled surface of the inner layer is formed with another surface layer; and the other surface layer has the same chemical composition as the surface layer.

(3) A titanium material for hot rolling, comprising: a base material containing industrial pure titanium or a titanium alloy; a surface layer joined to at least one of the rolled surfaces of the base material; and a welded portion joining the mother a material and a periphery of the surface layer; and the surface layer has a chemical composition different from the base material, and is, by mass%, B: 0.1 to 3.0%, and the balance: titanium and impurities; the fusion portion is the mother The interface between the material and the surface layer is interrupted by external air.

(4) The titanium material for hot rolling according to (3) above, wherein a surface layer other than the rolled surface of the base material is joined to another surface layer; and the other surface layer has the same chemical group as the surface layer. to make.

(5) The titanium material for hot rolling according to (3) or (4) above, wherein the base material comprises a directly cast flat embryo.

(6) The titanium material for hot rolling according to (5) above, wherein the directly cast flat embryo has at least a part of a surface thereof formed with a molten resolidified layer.

(7) The titanium material for hot rolling according to (6) above, wherein the chemical composition of the molten resolidified layer is different from the chemical composition of the center portion of the thickness of the directly cast flat embryo.

The titanium composite material according to the present invention has an inner layer containing industrial pure titanium or a titanium alloy and a surface layer having a chemical composition different from that of the inner layer, and therefore has the same degree as a titanium material composed of the same titanium alloy as a whole. Neutron occlusion, however, can be manufactured inexpensively.

1, 2‧‧‧ Titanium composite

3, 4‧‧‧ surface

5‧‧‧ inner layer

6‧‧‧ parent material (flat embryo)

7,8‧‧‧Materials (titanium plate)

9‧‧‧welding department

Fig. 1 is an explanatory view showing an example of the configuration of a titanium composite material according to the present invention.

Fig. 2 is a view showing an example of the structure of a titanium composite material according to the present invention. Illustrating.

Fig. 3 is an explanatory view schematically showing a state in which a titanium rectangular cast piece and a titanium plate are welded in a vacuum.

Fig. 4 is an explanatory view schematically showing a state in which a titanium plate is welded not only to the surface of the titanium rectangular cast piece but also to the side surface thereof.

Fig. 5 is an explanatory view showing a method of melting and resolidifying.

Fig. 6 is an explanatory view showing a method of melting and resolidifying.

Fig. 7 is an explanatory view showing a method of melting and resolidifying.

In order to solve the above problems, the inventors of the present invention have reduced the use amount of a specific alloying element which exhibits neutron blocking property by alloying only the surface layer of the titanium plate of the final product, and in order to suppress the manufacturing cost of the titanium material, As a result of intensive research, it was discovered that a base material containing industrial pure titanium or titanium alloy and a surface material having a chemical composition different from that of the base material were used to break the interface of the material from the outside air. A titanium material for hot rolling obtained by welding the base material and the surface layer. The titanium composite obtained by hot-working the titanium material for hot rolling can be a titanium material which is excellent in cost and excellent in sub-blocking property.

The present invention has been completed based on the above knowledge and insights. Hereinafter, the titanium composite material according to the present invention and the titanium material for hot rolling thereof will be described with reference to the drawings. In addition, in the following description, "%" of the content of each element means "mass%" unless it is especially dissatisfied.

Titanium composite 1-1. Overall composition

As shown in the first and second figures, the titanium composite materials 1 and 2 include an inner layer 5 containing industrial pure titanium or a titanium alloy, and a rolled surface formed on at least one of the inner layers 5 and having a different surface from the inner layer 5. The chemical composition of the surface layers 3, 4, and an intermediate layer (not shown) formed between the inner layer 5 and the surface layers 3, 4 and having a chemical composition different from that of the inner layer 5. Further, in the examples shown in Figs. 1 and 2, an example in which the surface layer is formed on one or both of the rolling faces of the inner layer 5 may be used, and the surface of the inner layer 5 may be other than the rolling surface ( In the examples shown in Figs. 1 and 2, other surface layers are provided on the side surface (not shown). Hereinafter, the surface layer, the inner layer, and the middle layer will be described in order.

If the thickness of the surface layer is too thin, the desired characteristics cannot be sufficiently obtained. On the other hand, if it is too thick, the ratio of the titanium alloy in the entire titanium composite material will increase, and the cost advantage will be reduced. Therefore, the thickness is set to 2 μm or more, and the ratio of the total thickness is set to 40% or less for each single-sided layer.

1-2. Surface layer (thickness)

In the surface layer, if the thickness of the surface layer that is in contact with the external environment is too thin, the neutron beam shielding effect cannot be sufficiently obtained. On the other hand, in the case where the surface layer is thick, the neutron line shielding effect can be improved, but the ratio of the titanium alloy in the entire material is increased, so the manufacturing cost is increased. The thickness of the surface layer is preferably 5 μm or more, and more desirably 10 μm or more. Relative titanium composite 1 The ratio of the thickness of the surface layer of the total thickness is set to 40% or less per layer, and more desirably 30% or less. Particularly good is set to 5~40%.

(chemical composition)

In the titanium composite material 1 according to the present invention, an alloying element is contained in order to provide a surface layer with a neutron shielding effect. The reasons for selecting the added elements and the reasons for limiting the range of additions are described in detail below.

B: 0.1~3.0%

In B, ¹⁰ B present 19.9%, this heat absorption cross section ¹⁰ B of the large-area neutron shielding neutrons great effect. When the B content is less than 0.1%, the neutron beam shielding effect cannot be sufficiently obtained, and if the B content is more than 3.0%, cracking during hot rolling and deterioration of workability may occur.

Here, the titanium alloy containing B can be produced by adding a boride such as B or TiB ₂ to titanium. In addition, if ¹⁰ B concentrated boron-containing material ( ¹⁰ B content is approximately 90% or more) such as H ₃ ¹⁰ BO ₃ or ¹⁰ B ₂ O ¹⁰ B ₄ C is used, the neutron shielding effect is large even if the B content is small. Therefore, it is extremely effective.

In the case of using H ₃ ¹⁰ BO ₃ , ¹⁰ B ₂ O, ¹⁰ B ₄ C, H and O are also concentrated in the alloy layer, but the removal of H from the material during heat treatment such as vacuum annealing does not become a problem. When O and C are 0.4 mass% or less or less and 0.1 mass% or less of the upper limit or less contained in the industrial pure titanium, the production can be carried out without problems.

The remainder other than the above is an impurity. As impurities, it can be impaired in the range of neutron-line occlusion, and other impurities mainly include Cr, Ta, Al, V, Cr, Nb, Si, Sn, Mn, Mo, and Cu as impurities in the mixture. In addition, it is a total of C, N, Fe, O, and H, which are common impurity elements, and the total amount is 5% or less.

(use)

A polyethylene material having a B content of 3.0 to 4.0% by mass and a sheet thickness of 10 to 100 mm is used in a facility for radiation therapy such as particle beam therapy or BNCT (boron neutron capture therapy). Further, in the nuclear energy related equipment, a stainless steel plate having a B content of 0.5 to 1.5% by mass and a plate thickness of 4.0 to 6.0 mm is used in the nuclear fuel storage frame. The titanium composite material 1 adjusted by using the B content and the thickness (the thickness of the B-concentrated layer) of the surface layer can exhibit characteristics equivalent to or higher than those of the above materials.

1-3. Inner layer

The inner layer 5 contains industrial pure titanium or a titanium alloy. For example, when industrial pure titanium is used for the inner layer 5, it is excellent in workability at room temperature as compared with a titanium material containing the same titanium alloy as a whole.

Further, the industrial pure titanium referred to herein includes one to four kinds of JIS standards, and the industrial pure titanium specified in Grades 1 to 4 of ASTM specifications and 3.7025, 3.7035, and 3.7055 of DIN specifications. In other words, the pure titanium for industrial use in the present invention contains, for example, C: 0.1% or less, H: 0.015% or less, and O: 0.4% or less, and N: 0.07% or less, Fe: 0.5% or less, and the rest of Ti.

Further, in addition to the specific properties, the titanium alloy may be used for the inner layer 5 when it is used for applications where strength is also required. By increasing the B content of the surface layer and the inner layer 5 being made of a titanium alloy, the alloy cost can be greatly reduced and high strength can be obtained.

The titanium alloy forming the inner layer 5 may be any one of an α type titanium alloy, an α + β type titanium alloy, and a β type titanium alloy, depending on the intended use.

Here, as the α-type titanium alloy, for example, a highly corrosion-resistant alloy (ASTM Grade 7, 11, 16, 26, 13, 30, 33 or a JIS species corresponding thereto or a small amount of a titanium material containing various elements) may be used. , Ti-0.5Cu, Ti-1.0Cu, Ti-1.0Cu-0.5Nb, Ti-1.0Cu-1.0Sn-0.3Si-0.25Nb, Ti-0.5Al-0.45Si, Ti-0.9Al-0.35Si, Ti -3Al-2.5V, Ti-5Al-2.5Sn, Ti-6Al-2Sn-4Zr-2Mo, Ti-6Al-2.75Sn-4Zr-0.4Mo-0.45Si, and the like.

As the α + β type titanium alloy, for example, Ti-6Al-4V, Ti-6Al-6V-2Sn, Ti-6Al-7V, Ti-3Al-5V, Ti-5Al-2Sn-2Zr-4Mo-4Cr, Ti can be used. -6Al-2Sn-4Zr-6Mo, Ti-1Fe-0.35O, Ti-1.5Fe-0.5O, Ti-5Al-1Fe, Ti-5Al-1Fe-0.3Si, Ti-5Al-2Fe, Ti-5Al-2Fe -0.3Si, Ti-5Al-2Fe-3Mo, Ti-4.5Al-2Fe-2V-3Mo, and the like.

Further, as the β-type titanium alloy, for example, Ti-11.5Mo-6Zr-4.5Sn, Ti-8V-3Al-6Cr-4Mo-4Zr, or the like can be used. Ti-10V-2Fe-3Mo, Ti-13V-11Cr-3Al, Ti-15V-3Al-3Cr-3Sn, Ti-6.8Mo-4.5Fe-1.5Al, Ti-20V-4Al-1Sn, Ti-22V-4Al Wait.

However, if the 0.2% proof endurance of the inner layer 5 is more than 1000 MPa, the workability is deteriorated, for example, cracking occurs during bending. Therefore, it is desirable that the titanium used for the inner layer 5 and the titanium alloy have a 0.2% proof force of 1000 MPa or less.

1-4. Middle layer

The titanium composite of the present invention has an intermediate layer between the inner layer and the surface layer. In other words, the titanium material for hot rolling described later is obtained by attaching a base material to a surface layer and welding the periphery thereof, but in the subsequent hot rolling heating and heat treatment steps after cold rolling, the base material and the surface layer are formed. Diffusion occurs at the interface of the material, and when finally processed into a titanium composite, an intermediate layer is formed between the inner layer from the base material and the surface layer from the surface layer. This intermediate layer has a chemical composition different from the chemical composition of the base material. The intermediate layer is strongly bonded to the inner layer and the surface layer metal. Further, since a continuous element gradient is generated in the intermediate layer, the difference in strength between the inner layer and the surface layer can be alleviated, and cracking during processing can be suppressed.

Further, the thickness of the intermediate layer can be measured by EPMA or GDS. More detailed measurements can be made if GDS is used. In the case of GDS, after the surface layer is removed by some degree of polishing, the thickness of the intermediate layer can be measured by performing GDS analysis from the surface in the depth direction. The intermediate layer is defined as the C _MID from the increased content of the base material (the content of the element contained in the base material, the content of the element contained in the base material, and the increase from the content of the base material). When the average of the increased content of the surface layer portion is C _AVE , it is in the region of 0 < C _MID ≦ 0.8 × C _AVE .

The thickness of this intermediate layer is set to 0.5 μm or more. On the other hand, if the thickness of the intermediate layer is too large, the alloy layer of the surface layer corresponding thereto becomes thin, and there is a case where the effect cannot be expressed. Therefore, the upper limit should be set to 15 μm.

2. Titanium for hot rolling

The titanium material for hot rolling of the present invention is supplied with a material for hot intercalation processing (a cast piece of a flat embryo, a medium embryo, a small embryo, etc.), and is processed into a cold process, a heat treatment, etc. Titanium composite. Hereinafter, the titanium material for hot rolling of the present invention will be described with reference to the drawings. In the following description, the "%" of the content of each element means "% by mass".

2-1. Overall composition

Fig. 3 is an explanatory view schematically showing a base material (titanium rectangular cast piece, flat blank) 6 and a surface layer (titanium plate) 7 welded together in a vacuum, and Fig. 4 is not only a base material (titanium) The surface of the rectangular slab, the flat slab 6 (rolled surface), and the side surface (the surface other than the rolling surface) are also schematically shown by welding the surface materials (titanium plates) 7 and 8 and bonding them together.

In the present invention, as shown in Figs. 3 and 4, the titanium plates 7 and 8 containing an alloying element capable of exhibiting neutron blocking properties are bonded to the surface of the flat metal 6 as a base material, and then joined by a hot-rolled cladding method. And the surface of the titanium composite 1, 2 Alloying.

In the case of manufacturing the titanium composite material 1 shown in Fig. 1, as shown in Fig. 3, the titanium plate 7 can be bonded to the single side of the flat embryo 6 in a vacuum, and the other is the flat embryo 6 Hot rolling is performed by attaching the titanium plate 7 to one side.

As shown in Fig. 4, in addition to the single side of the flat blank 6, the titanium plate 7 can be attached to the other side. Thereby, the occurrence of hot rolling defects in the hot rolling step can be suppressed as described above.

Further, in the case of producing the titanium composite material 2 shown in Fig. 2, as shown in Fig. 4, a plate containing an alloy element may be bonded to the two rolled surfaces of the flat blank 6.

Further, as shown in Fig. 4, the side surface of the flat blank 6 which is the edge side during hot rolling can be welded to the titanium plate 8 which is the same as the rolled surface in the vacuum.

That is, in the hot rolling, usually, the flat embryo 6 is subjected to rolling, and at least a part of the side surface of the flat blank 6 is drawn back to the surface side of the hot rolled sheet. Therefore, if the surface layer of the side surface of the flat blank 6 is coarse or there are many defects, the surface of the hot rolled sheet near the both ends in the width direction may have a surface flaw. Therefore, since the titanium plate 8 is bonded and welded in a vacuum in the side surface of the flat blank 6, it is possible to effectively prevent surface flaws on the surface near the both ends in the width direction of the hot rolled sheet.

Moreover, the amount of twist of the side surface of the flat blank 6 during hot rolling varies depending on the manufacturing method, but is usually about 20 to 30 mm, so that it is not necessary to completely attach the titanium plate 8 to the side of the flat embryo 6, and the manufacturing method is A considerable amount of the back is attached to the titanium plate 8.

2-2. Surface material

When the titanium composite materials 1 and 2 are produced, in order to remove the oxide layer formed by hot rolling, the hot rolling is performed by a sandblasting-pickling step. However, at this step, if the surface layer formed by the hot rolled cladding is removed, the desired neutron blocking property cannot be expressed.

Further, if the thickness of the surface layers of the titanium composite materials 1 and 2 is too thin, the target neutron-shielding property cannot be expressed. On the other hand, if the thickness of the surface layer is too thick, the manufacturing cost will increase accordingly. Since the titanium composite materials 1 and 2 have a thickness of the surface layer to be used for the purpose of use, the thickness of the titanium plates 7 and 8 used as the material is not particularly limited, but the thickness of the flat embryo 6 is 5 to 40%. The scope is appropriate.

As the surface layer (titanium plate), a titanium plate having a specific chemical composition described in the item of the surface layer of the above-mentioned titanium composite material is used. It is particularly preferable that the chemical composition of the titanium plate is adjusted to a component containing a specific element in order to suppress breakage of the plate due to hot rolling, in the same manner as the above-mentioned base material. Pay special attention to the following points.

As the surface layer, a titanium alloy sheet containing 0.1% or more and 3% or less of B is used. Specifically, it is desirable that the chemical composition of the surface layer is adjusted to have a content of 0.1% or more in accordance with the same composition as the above-mentioned base material in order to suppress breakage of the sheet due to hot rolling. A component of B below 3%. Further, in order to satisfactorily ensure the workability between the hot and cold compartments, it may be a Ti-0.1 to 3% B alloy.

The B-containing titanium alloy sheet can be produced by adding a boride such as B or TiB ₂ to titanium. Further, when ¹⁰ B concentrated boron-containing material such as H ₃ ¹⁰ BO ₃ , ¹⁰ B ₂ O, or ¹⁰ B ₄ C is used (the content of ¹⁰ B is approximately 90% or more), even if the amount of B added to the surface layers 3 and 4 is small, The titanium composites 1, 2 still have a large neutron line shielding effect and are extremely effective.

In the case of using H ₃ ¹⁰ BO ₃ , ¹⁰ B ₂ O, and ¹⁰ B ₄ C, H, O, and C in the alloy layer are also concentrated, but H is removed from the material during heat treatment such as vacuum annealing. It is not a problem. If O or C is 0.4% O or less and 0.1% C or less of the upper limit of the industrial pure titanium, the production can be carried out without problems.

2-3. Base metal (flat embryo)

As the base material, industrial pure titanium or a titanium alloy described in the item of the inner layer of the titanium composite material is used. In particular, the base material should be directly cast flat embryos. A direct cast flat embryo can be formed by melting a resolidified layer on at least a portion of the surface. Further, in the case where the surface of the directly cast flat embryo is subjected to a melt re-solidification treatment, a specific element is added to form a molten re-solidified layer having a different thickness from the center portion of the directly cast flat embryo. chemical components.

2-4. Welding joint

On the surface of the flattened blank 6 as a rolled surface, after bonding the titanium plate 7 containing the alloying element, at least the surrounding portion is welded by the welded portion 9 in the vacuum container, whereby the flat blank 6 and the titanium plate 7 are The vacuum is sealed between the 8 and the outside air, and the flat embryo 6 is bonded to the titanium plates 7, 8 by rolling. Flat embryo 6 The welded portion to which the titanium plates 7 and 8 are bonded to each other is formed by fusing the interface between the flat blank 6 and the titanium plates 7 and 8 from the atmosphere, for example, as shown in Figs. 3 and 4 .

Titanium is an active metal, so if placed in the atmosphere, the surface will form a strong passive film. It is impossible to remove the oxidized concentrated layer on the surface portion. However, unlike stainless steel or the like, oxygen is easily dissolved in titanium. Therefore, if it is sealed in a vacuum and heated without supplying oxygen from the outside, oxygen on the surface diffuses to the inside and solidifies, so the surface is blunt. The membrane will be destroyed. Therefore, the flat blank 6 and the titanium plates 7 and 8 on the surface thereof can be completely adhered by the hot rolling cladding method without causing inclusions or the like therebetween.

Further, when the flat embryo 6 is used as the original embryo after casting, it is caused by coarse crystal grains generated during solidification, and surface flaws occur in the subsequent hot rolling step. On the other hand, if the titanium plates 7 and 8 are bonded to the rolled surface of the flat blank 6 as in the present invention, since the bonded titanium plate 7 has a fine structure, the surface flaw of the hot rolling step can be suppressed.

3. Method for manufacturing titanium material for hot rolling 3-1. Manufacturing method of base material

The base material of the titanium material for hot rolling is usually produced by decomposing the ingot into a flat embryo or a small embryo shape, and then cutting and finishing. Further, in recent years, there has been a case where a rectangular flat embryo which can be directly hot rolled is produced for hot rolling in the production of an ingot. In the case of manufacturing by decomposition, the surface is formed to be relatively flat due to decomposition, and it is easy to uniformly distribute the material containing the alloying elements, and it is easy to make the elemental distribution of the alloy phase uniform.

On the other hand, in the case where an ingot (direct cast flat blank) which is directly formed into a shape of a material for hot rolling is used as a base material at the time of casting, since the cutting finishing step can be omitted, it can be manufactured more inexpensively. . Moreover, after the ingot is manufactured and the surface is cut and finished, it is expected to have the same effect in the case of production by decomposition. In the present invention, if an alloy layer is formed in the surface layer stably, an appropriate material can be selected in accordance with the condition.

Preferably, for example, after the flat embryos are combined and welded, they are heated at 700 to 850 ° C for 10 to 30% of the joining and rolling, and then heated at a β domain temperature for 3 to 10 hours to diffuse the base material. After the surface layer, hot rolling is performed. This is because, by hot rolling at the temperature of the β domain, the deformation resistance is lowered and it is easy to roll.

A direct-cast flat embryo used as a base material may be formed by melting and re-solidifying a layer on at least a part of the surface. Further, in the case where the surface of the directly cast flat embryo is subjected to a melt re-solidification treatment, a specific element is added to form a molten re-solidified layer having a different thickness from the center portion of the directly cast flat embryo. chemical components. Hereinafter, the melt resolidification treatment will be described in detail.

Figs. 5 to 7 are explanatory views each showing a method of melting and resolidifying. As a method of melting and resolidifying the surface of the base material of the titanium material for hot rolling, including laser heating, plasma heating, induction heating, electron beam heating, etc., any method is feasible. Especially in the case of electron beam heating, since it is carried out in a high vacuum, even if pores or the like are formed in the layer during the melt resolidification treatment, since it is a vacuum, it can be rolled by then And it is harmless.

Further, since the energy efficiency is high, it can be deeply melted even if it is treated in a large area, and therefore it is particularly suitable for the production of a titanium composite material. The degree of vacuum in the case of melting in a vacuum is satisfactorily a higher degree of vacuum of 3 × 10 ^-3 Torr or less. Moreover, the number of times of melting and resolidifying the surface layer of the titanium material for hot rolling is not particularly limited. However, the more the number of times, the longer the processing time leads to an increase in cost, so that it is satisfactory one to two times.

The melt re-solidification method of the surface layer is carried out as shown in Fig. 5 in the case of a rectangular flat embryo. Specifically, for the outer surface of the rectangular flat blank 10, at least the wide sides 10A, 10B which are the rolling surfaces of the hot rolling step (the surface in contact with the hot rolling rolls) are irradiated with electron beams, and only the The surface layer of the surface is melted. Here, first, the surface 10A of one of the two faces 10A and 10B is implemented.

Here, as shown in Fig. 5, the area of the irradiation region 14 of the electron beam which is directed to the electron beam irradiation gun 12 of the face 10A of the rectangular cast piece 10 is usually additionally larger than the entire area of the face 10A to be irradiated. Since the electron beam irradiation gun 12 is continuously moved or the rectangular casting piece 10 is continuously moved, the electron beam irradiation is performed. In this illumination region, the beam current is formed by adjusting the focus of the electron beam or by using an electromagnetic lens to make a small beam of Oscillation, whereby the shape or area can be adjusted.

Further, as shown by an arrow A in Fig. 5, the following description will be made for the case where the electron beam irradiation gun 12 is continuously moved. Moreover, the moving direction of the electron beam irradiation gun is not particularly limited, and generally is a rectangular casting. The longitudinal direction of the sheet 10 (usually the casting direction D) or the width direction (usually the direction perpendicular to the casting direction D) continuously moves, in the case of the width W of the aforementioned irradiation region 14 (in the case of a circular beam or a beam current, The diameter W) is continuously irradiated in a strip shape. Further, the irradiated gun 12 is continuously moved in the opposite direction (or the same direction) with respect to the adjacent unilluminated strip-shaped region, and the electron beam irradiation is performed in a strip shape. Depending on the situation, a plurality of illuminating guns may be used, and electron beam irradiation may be simultaneously performed on a plurality of regions. In Fig. 5, the case where the rectangular beam is continuously moved in the longitudinal direction of the rectangular cast piece 10 (usually in the casting direction D) is shown.

When the surface (face 10A) of the rectangular titanium slab 10 is irradiated with an electron beam by such a surface heat treatment step, and the surface thereof is heated to be molten, as shown in the center of the sixth figure, the rectangular titanium slab is shown. The surface layer of 10A of 10 is most melted in response to the depth of heat input. However, the depth from the vertical direction of the irradiation direction of the electron beam is not constant as shown in Fig. 7, and the central portion of the electron beam irradiation is the maximum depth, and the thickness of the end portion of the strip is reduced to become the lower convex portion. The curved shape.

Further, the region closer to the inner side of the cast sheet than the molten layer 16 is heated, and the temperature rises due to the influence of the heat of the electron beam irradiation, and becomes a portion of the temperature above the β-deformation point of pure titanium (heat-affected layer = The HAZ layer is metamorphosed into a beta phase. In the same manner, the region which is transformed into the β phase due to the thermal influence by the electron beam irradiation in the surface heating treatment step is the same as the shape of the molten layer 16 and has a curved shape which is convex downward.

By using the surface layer and the material containing the alloying element of interest The melt resolidification is carried out to alloy the surface layer of the hot rolling material to form an alloy layer having a chemical composition different from that of the base material. As the material used at this time, one or more of a powder, a small piece, a wire, a film, a chip, and a mesh can be used. The component and the amount of the material disposed before the melting are defined as a component of the element-concentrated region which is melt-solidified together with the surface of the material as a target component.

However, if the material added is too large, it will cause segregation of the alloy composition. Further, if the segregation of the alloy component is present, the desired performance may not be sufficiently exhibited, or the deterioration may occur early. Therefore, it is important that the heated portion of the surface of the titanium base material is in a molten state, and the alloy material becomes the size of the melting end. Further, it is important to arrange the alloy material in advance on the surface of the titanium base material in consideration of the shape and the width of the molten portion at a specific time. However, in the case where the irradiation position is continuously moved by using the electron beam, since the molten portion is stirred while continuously moving together with the molten titanium and the alloy, the alloy material does not necessarily have to be continuously arranged in advance. In addition, it is of course necessary to avoid the use of alloy materials having an extremely high melting point than the melting point of titanium.

After the melt resolidification treatment, it is preferably maintained at a temperature of 100 ° C or more and less than 500 ° C for 1 hour or more. After melting and re-solidification, if it is rapidly cooled, the surface layer portion is slightly broken due to the strain at the time of solidification. In the subsequent hot rolling step or cold rolling step, the fine fracture is used as a starting point, and the neutron blocking property such as the occurrence of peeling of the surface layer and the occurrence of a thinned portion of the local alloy layer may be deteriorated. Moreover, when the internal oxidization is caused by the fine rupture, it is necessary to remove it by the pickling step, and the condensation is further reduced. The thickness of the gold layer. By holding at the above temperature, fine cracking of the surface can be suppressed. Moreover, at this temperature, atmospheric oxidation hardly occurs even if it is maintained in the atmosphere.

The titanium material for hot rolling can be produced by attaching a titanium plate containing a specific alloy component to the surface of the base material having the surface layer portion formed by the melt resolidification treatment.

3-2. Hot rolling cladding method

The titanium material for hot rolling is preferably joined to the titanium plates 7, 8 by a hot-rolled cladding method.

As shown in the third and fourth figures, the titanium plates 7 and 8 containing the alloying elements exhibiting neutron blocking properties are attached to the surface layer of the flat embryo 6, and then joined by a hot-rolled cladding method, whereby the titanium composite material is joined. The surface layer is alloyed. That is, the titanium plate 7 containing the alloying elements is attached to the surface of the flat surface of the flat blank 6 as a rolled surface, preferably in a vacuum container, at least the surrounding portion is welded by the welded portion 9, thereby the flat embryo 6 and the titanium plate 7 are vacuum-sealed, and the flat blank 6 is bonded to the titanium plate 7 by rolling. The titanium plate 7 is welded to the slab 6 so that the atmosphere between the squash 6 and the titanium plate 7 is not intruded, for example, as shown in Figs. 3 and 4, the whole circumference is welded.

Titanium is an active metal, so if placed in the atmosphere, the surface will form a strong passive film. It is impossible to remove the oxidized concentrated layer on the surface portion. However, unlike stainless steel and the like, oxygen is easily dissolved in titanium, and if it is sealed in a vacuum and heated without supplying oxygen from the outside, oxygen on the surface diffuses to the inside and solidifies, so that the surface is formed into a passive state. Membrane will disappear Off. Therefore, the flat blank 6 and the titanium plate 7 on the surface thereof can be completely adhered by the hot-rolled cladding method without causing inclusions or the like therebetween.

Further, if the flat embryo 6 is used as a raw embryo after casting, it is caused by coarse crystal grains which are formed during solidification, and surface flaws occur in the subsequent hot rolling step. On the other hand, when the titanium plate 7 is bonded to the rolled surface of the flat blank 6 as in the present invention, since the bonded titanium plate 7 has a fine structure, the surface flaw in the hot rolling step can be suppressed.

As shown in Fig. 3, not only the single side of the flat blank 6, but also the titanium plate 7 may be bonded to both sides thereof. Thereby, the occurrence of hot rolling in the hot rolling step can be suppressed as described above. In the hot rolling, usually, the flat embryo 6 is rolled, and at least a part of the side surface of the flat blank 6 is drawn back to the surface side of the hot rolled sheet. Therefore, if the surface layer of the side surface of the flat blank 6 is coarse or has many defects, the surface near the both ends in the width direction of the hot rolled sheet may have a surface flaw. Therefore, as shown in Fig. 4, it is preferable to form the side surface of the flat blank 6 on the edge side at the time of hot rolling, and also to splicing the titanium plate 8 of a contract type similarly to the rolled surface. Thereby, it is possible to effectively prevent surface flaws on the surface near both ends in the width direction of the hot rolled sheet. This fusion is preferably carried out in a vacuum.

Further, the amount of the side back of the flat embryo 6 during hot rolling differs depending on the manufacturing method, and is usually about 20 to 30 mm. Therefore, it is not necessary to completely attach the titanium plate 8 to the side of the flat embryo 6, and it is only equivalent. The titanium plate 8 may be attached to the portion of the manufacturing method. By hot rolling, the composition from the base material can be contained in the interior of the titanium composite by performing high-temperature annealing for a long time. It can be exemplified by, for example, 30 hours of heat at 700 to 900 ° C. deal with.

A method of welding the flat blank 6 and the titanium plates 7, 8 in a vacuum, including electron beam welding or plasma welding, and the like. It is particularly desirable to carry out the electron beam welding under high vacuum, whereby a high vacuum can be set between the flat blank 6 and the titanium plates 7, 8. Desirably, the degree of vacuum in the case of the titanium plates 7,8 fused in vacuo, to the following 3 × 10 ^-3 Torr of a higher degree of vacuum.

Further, the welding of the flat blank 6 and the titanium plate 7 does not necessarily have to be performed in a vacuum container. For example, a vacuum suction hole may be provided in advance in the titanium plate 7, and the titanium plate 7 and the flat blank 6 may be overlapped. The vacuum is used to evacuate the flat blank 6 and the titanium plate 7, and the flat blank 6 is welded to the titanium plate 7, and the vacuum suction hole is closed after welding.

As the cladding, the titanium plates 7 and 8 having the intended alloying elements are used on the surface of the flat blank 6, and the thickness or chemical composition of the surface layer is formed by hot-rolling cladding to form an alloy layer on the surface layers of the titanium composites 1 and 2. It depends on the thickness of the titanium plates 7, 8 before the bonding or the distribution of the alloying elements. Of course, in the production of the titanium plates 7, 8, in order to obtain the final necessary strength and ductility, annealing treatment is performed in a vacuum atmosphere or the like, thereby causing diffusion at the interface, and a concentration gradient is generated in the vicinity of the interface in the depth direction.

However, the diffusion distance of the element caused by the final annealing step is about several μm, which is not the overall diffusion of the thickness of the alloy layer, and has no effect on the concentration of the alloying element in the vicinity of the surface layer which is particularly important for the neutron blocking performance.

Therefore, the uniformity of the alloy composition of the titanium plates 7 and 8 as a whole is It is closely related to the performance of the stability of the characteristics. In the case of the hot-rolled cladding, since the titanium plates 7 and 8 manufactured by the products can be used, the thickness accuracy of the alloy is not easily controlled, and the segregation of the alloy components can be easily controlled, and the titanium composite materials 1 and 2 having the surface layer can be manufactured. This surface layer has a uniform thickness and chemical composition after manufacture, and can exhibit stable properties.

Further, as described above, since no inclusions are formed between the surface layers of the titanium composite materials 1 and 2 and the inner layer 5, they do not become a starting point of cracking or fatigue, etc., in addition to the adhesion.

3. Method for manufacturing titanium composite material

It is important that the alloy layer formed by attaching the titanium plate to the surface of the flat embryo is left as a final product residue, and it is therefore necessary to suppress the loss of the oxide film or the surface layer caused by the surface flaw as much as possible. Specifically, after considering the characteristics or capabilities of the equipment used in the production, the technical solutions on the hot rolling step described below are optimized and appropriately employed.

4-1. Heating step

When the material for hot rolling is heated, the loss of the oxide film can be suppressed to be low by heating at a low temperature for a short period of time. However, since the heat conduction of the titanium material is small, if the inside of the flat embryo is hot-rolled at a low temperature, the inside is liable to occur. The disadvantage of cracking is therefore optimized in accordance with the performance or characteristics of the furnace to be used to minimize the occurrence of the film.

4-2. Hot rolling step

Also in the hot rolling step, if the surface temperature is too high, a large amount of film is formed during the passage, and the oxide film loss is increased. On the other hand, if the oxide film loss is too low, the surface enthalpy becomes easy to occur, so it is necessary to remove it by pickling in a subsequent step, and it is desirable to carry out heat treatment by suppressing the temperature range of the surface enthalpy. Rolling. Therefore, it is desirable to perform rolling at an optimum temperature range. Further, since the surface temperature of the titanium material is lowered during the rolling, it is satisfactory that the cooling of the rolls during the rolling is minimized, and the decrease in the surface temperature of the titanium material is suppressed.

4-3. Pickling step

The hot rolled sheet has an oxide layer on its surface and thus has a step of removing the oxide layer in a subsequent step. Titanium is generally mainly used after sand blasting to remove the oxide layer by acid washing with a solution of nitric acid. Further, depending on the situation, there is a case where the surface is ground by grinding with a grindstone after pickling. After the film is removed, it may be a two-layer or three-layer structure composed of the inner layer and the surface layer of the base material and the surface layer portion of the titanium material for hot rolling.

Since the film formed by the hot rolling step is thick, it is usually treated as a pickling treatment to remove a part of the surface film before the pickling treatment, and a crack is formed on the surface, and the liquid is soaked to the crack in the subsequent pickling step. So that one part of the base material is also removed. At this time, it is important to perform a weak blasting treatment which does not cause cracks on the surface of the base material, and it is necessary to select an optimum blasting condition in accordance with the chemical composition of the surface of the titanium material. Specifically, for example, by optimizing the selection or projection speed of the appropriate projecting material (adjustable by the rotational speed of the impeller), it is optional to be absent on the base metal. The condition of the crack. The optimization of these conditions differs depending on the characteristics of the titanium plate to which the surface of the flat embryo is attached. Therefore, the optimum conditions may be determined in advance.

Hereinafter, the present invention will be more specifically described based on the examples, but the present invention is not limited by the examples.

[Example 1]

Hereinafter, the present invention will be more specifically described with reference to the embodiments.

The sub-line shielding plates shown in Figs. 1 and 2 and Table 1 were produced by using the hot-rolled cladding layers shown below using the flat blanks 6 and the titanium plates 7 and 8 shown in Figs. 3 and 4 as materials.

First, the titanium ingot 6 as a material is produced by electron beam melting (EB melting), plasma arc melting (plasma melting) using a rectangular mold, or by VAR melting using a cylindrical mold. The size of the ingot 6, the cylindrical ingot 6 is 1200 mm in diameter × 2500 mm in length, and the rectangular ingot 6 is 100 mm in thickness × 1000 mm in width × 4,500 mm in length, and the type is pure titanium JIS, JIS 2, JIS 3, Ti-1Fe-0.35O, Ti- 0.5Cu, Ti-1Cu, Ti-1Cu-0.5Nb, Ti-5Al-1Fe, Ti-3Al-2.5V, Ti-3Al-5V.

The cast ingot 6 is almost in the original state, or after the black skin on the surface of the ingot 6 is cut, the titanium plate 7 is bonded. The other ingots 6 are cut after the block rolling, and the titanium plates 7 are bonded together.

The bonding of the titanium plate 7 is to overlap (coat) the Ti-B alloy sheets of the same size and the thickness of the ingot or the flat blank 6, and the ends of the titanium plate 7 are welded by electron beams ( The vacuum is performed at a vacuum of about 3 × 10 ^-3 Torr or less, and the titanium plate 7 and the ingot (or flat embryo) 6 are sealed in a vacuum state.

The bonding of the alloy sheets is mainly performed on the rolled surface, and the two-layer structure which is implemented only on one surface and the three-layer structure on both sides are produced. For the surface layer (B concentrated layer) 3, 4, the ratio of each single-sided layer in the total thickness of the final product is shown in Table 1, and in the three-layer structure, it is adjusted to the two surfaces B. The concentrated layers have the same thickness. The titanium plate 7 used in the board bonding is a Ti-B alloy plate which is added by adding boron (H ₃ ¹⁰ BO ₃ , ¹⁰ B ₂ O ¹⁰ B ₄ C) concentrated beforehand using TiB ₂ or ¹⁰ B. The molten ingot is produced by hot rolling. Further, after the hot rolling, the Ti-B alloy sheet is subjected to a peeling film by a continuous pickling line containing nitric acid.

The flat metal 6 was heated at 800 ° C for 240 minutes using an iron steel equipment, and then hot rolled to produce strip-shaped rolls (titanium composite materials) 1 and 2 having a thickness of about 4 mm. By this hot rolling, the surface layers of the titanium composite materials 1 and 2 were formed into a Ti-0.1 to 3.8% B alloy.

In the present embodiment, the case where the flat embryo 6 is made of a titanium alloy is used. In this case as well, the bonded titanium plate 7 is made of a Ti-0.1 to 3.8% B alloy containing only Ti and B.

The strip rolls 1, 2 after hot rolling were peeled off by a continuous pickling line containing nitric acid, and then visually observed for the occurrence of cracking. Further, the method of measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is to take a part of the hot-rolled sheet (for the front end, the center, and the rear end in the longitudinal direction) Three parts were cut out from the center of the width direction, and the obtained material was subjected to SEM/EDS analysis to obtain the ratio of the B-concentrated layer of the relative thickness and the B concentration of the B-concentrated layer (observation) The average value among the parts).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

Further, the evaluation of the neutron line shielding effect was carried out using Am-Be (4.5 MeV) as a line source, and a test piece of 500 mm × 500 mm × 4 mm thick was fixed at a position of 200 mm from the line source. The detector is placed at a position of 300 mm from the line source. The peak value of the object energy is measured by measuring the radiation equivalent of the industrial pure titanium JIS type 1 and the test piece of the control test piece, and the ratio of the value of the neutron line is evaluated. The industrial pure titanium JIS 1 type has a sub-line shielding effect of 1, and the value of each test piece is described).

The results are summarized in Table 1.

In the comparative examples and examples shown in No. 1 to No. 8, the case of the original EB melting ingot (flat embryo 6) after casting was used.

In the comparative example of No. 1, as the titanium plate 7, one type of pure titanium JIS of the same type as the flat embryo 6 was used. The hot rolled sheet did not rupture, and no crack occurred in the bending test.

The comparative example of No. 2 is a case where the intermediate layer is thin. Part of the hot rolled sheet is broken, and the bending test also has a high incidence of cracking.

The comparative example of No. 3 is a case where the thickness ratio of the surface layers 3 and 4 exceeds 40%. Part of the hot rolled sheet was broken, and the incidence of cracking in the bending test was also high.

The examples of Nos. 4 to 7 were evaluated by changing the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the example of No. 8, the case where not only the rolled surface but also the side surface in the longitudinal direction was bonded to the alloy sheet was carried out. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is performed. No cracks occurred. Further, since the alloy sheet is bonded to the side surface in the longitudinal direction, the surface flaw due to the end portion in the width direction of the side surface is also reduced.

In the examples of No. 9 to 11, the plasma-infused original ingot after casting is used, and the type, layer structure, and surface layer 3 of the inner layer 5 are respectively changed. The case where the thickness ratio or the B content of 4 is evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of Nos. 12 to 14, the black skin surface of the EB melting ingot was cut and used, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3 and 4, or the B content were changed and evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 15 to 17, the black skin surface of the plasma melting ingot was cut and used, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3 and 4, or the B content were changed to evaluate the case. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 18 to 20, the various ingots were rolled and the surface was cut and reused, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content were respectively evaluated. The situation. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the embodiment of No. 21 to 23, after the various ingots are forged, the surface is cut and reused, and the type and layer structure of the inner layer 5 are respectively changed. The case where the thickness ratio or the B content of the surface layer 3, 4 was evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the embodiment shown in No. 24 to 37, the VAR ingot is rolled and the surface is cut and used, and various titanium alloys are used as the inner layer 5, and the layer structure and the surface layer 3 and 4 are respectively changed. The case where the thickness ratio or the B content is evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in the alloy of the inner layer 5 in the example of the present invention, when the tensile test was carried out on a JIS13B test piece having a thickness of 1.5 mm, the 0.2% proof stress was found to be 1000 MPa or less.

Further, as a result of the evaluation by the above method, the neutron line shielding effect cannot be confirmed in the comparative example of No. 1, but the neutron shielding effect of any of the examples of Nos. 4 to 37 is 1 or more, and it can be confirmed. Neutron line shadowing effect.

Further, the stainless steel plate (4 mm thick) having a B content of 0.5% used in the nuclear fuel storage rack has a neutron shielding effect of 23.7, and the examples of No. 11, 13, and 17 can be made higher than the stainless steel plate. Strand shading effect.

[Example 2]

In Table 2, the neutron shielding sheets are shown as the respective examples (examples of the present invention) by the following methods.

The slab 6 to which the sheet was bonded was subjected to the same procedure as in Example 1, and was subjected to hot rolling at 800 ° C for 240 minutes using an iron steel apparatus to produce a strip roll (titanium composite) having a thickness of about 20 mm. 1, 2. By this hot rolling, the surface layers of the titanium composite materials 1 and 2 were formed into a Ti-0.1 to 3.8% B alloy. The strip-shaped rolls 1 and 2 after hot rolling were peeled off through a continuous pickling line containing nitric acid, and then visually observed for the occurrence of cracking. In addition, the method of measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is to cut one part of the hot-rolled sheet (three portions from the front end, the center, and the rear end in the longitudinal direction, respectively, taken from the center portion in the width direction). The material obtained by the polishing was subjected to SEM/EDS analysis to determine the ratio of the B-concentrated layer having a relative thickness and the B concentration of the B-concentrated layer (using the average value among the observed portions).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

Further, in the evaluation of the neutron line shielding effect, Am-Be (4.5 MeV) was used as the line source, and a test piece of 500 mm × 500 mm × 20 mm thick was fixed at a position of 200 mm from the line source. The detector is placed at a position 300 mm from the line source, and the peak value of the object energy is in the control test piece. Industrial pure titanium JIS type 1 and test piece were measured for radiation equivalent, and the ratio of the ratio was measured, and the neutron line shielding effect was evaluated (in the case of industrial pure titanium JIS, the sub-line shielding effect is 1, and the value of each test piece is described) .

The results are shown in Table 2.

In the comparative examples and examples of No. 38 to No. 42, the case of the original EB melting ingot (flat embryo 6) after casting was used.

In the comparative example of No. 38, the case where the pure titanium JIS of the same kind as the flat embryo 6 was used as the titanium plate 7 was used. The hot rolled sheet did not rupture, and no crack occurred in the bending test.

The comparative example of No. 39 is a case where the intermediate layer is thin. Part of the hot rolled sheet is broken, and the bending test also has a high incidence of cracking.

The examples of No. 40 to 42 were evaluated by changing the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of Nos. 43 to 45, the slurry was melted in the original state after casting, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content were changed. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of Nos. 46 to 48, the surface of the black skin of the EB melting ingot was cut and used, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content were changed and evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the example of No. 49-51, the black skin surface of the plasma melting ingot is cut and reused, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content are respectively changed for evaluation. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 52-54, the various ingots are rolled and then the surface is cut and used, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content are changed. The situation of the assessment. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

The embodiment of No. 55-57 is a case where the surface is cut and used after forging the various ingots, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content are changed. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in the examples of Nos. 40 to 57, the neutron line shielding effect can be confirmed regardless of the case where the sub-shading effect is 1 or more.

[Example 3]

In Table 3, the neutron shielding sheets are produced by the following methods as examples (invention examples).

The slab 6 to which the sheet was bonded was subjected to the same procedure as in Example 1, and was subjected to hot rolling at 800 ° C for 240 minutes using an iron steel apparatus to produce a rolled roll (titanium composite) having a thickness of about 5 mm. 1, 2. Then, cold rolling was performed to form a titanium plate having a thickness of 1 mm, and as an annealing treatment, heat treatment was carried out by heating to 600 to 750 ° C in a vacuum or an inert gas atmosphere for 240 minutes. The cold-rolled sheet was visually observed for the occurrence of cracking in the surface inspection step after annealing. Further, the method of measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is to cut one part of the cold-rolled sheet (for the three portions of the front end, the center, and the rear end in the longitudinal direction, respectively, taken from the center portion in the width direction). The material obtained by the polishing was subjected to SEM/EDS analysis to determine the ratio of the B-concentrated layer having a relative thickness and the B concentration of the B-concentrated layer (using the average value among the observed portions).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

Further, in the evaluation of the shielding effect of the neutron beam, Am-Be (4.5 MeV) was used as the line source, and a test piece of 500 mm × 500 mm × 1 mm thick was fixed at a position of 200 mm from the line source. The detector is placed at a position of 300 mm from the line source. The peak value of the object energy is measured by measuring the radiation equivalent of the industrial pure titanium JIS type 1 and the test piece of the control test piece, and the ratio of the value of the neutron line is evaluated. Industrial pure titanium JIS1 The sub-line shading effect is 1, and the value of each test piece is described).

The results are summarized in Table 3.

In the comparative examples and examples of No. 58 to No. 63, the case of the original EB melting ingot (flat embryo 6) after casting was used.

In the comparative example of No. 58, the titanium plate 7 was used as one type of pure titanium JIS of the same type as the flat embryo 6. The cold rolled sheet did not break, and no crack occurred in the bending test.

The comparative example of No. 59 is a case where the B content of the surface layers 3 and 4 exceeds 3.0%. The cold rolled sheet partially ruptured, and the bending test also has a high incidence of rupture.

The comparative example of No. 60 is a case where the thickness ratio of the surface layers 3 and 4 exceeds 40%. The cold rolled sheet partially ruptured, and the bending test also has a high incidence of rupture.

The examples of Nos. 61 to 63 were evaluated by changing the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold-rolled sheets, and the bending test is also performed. No cracking occurred.

The examples of Nos. 64 to 66 were evaluated by using a plasma-deposited ingot after casting, and changing the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold-rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 67 and 68, the black skin surface of the EB melting ingot or the plasma melting ingot is cut and used, and the inner layer 5 is changed separately. The case where the class, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content are evaluated. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 69 to 71, the various ingots were rolled and the surface was cut and reused, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content were respectively evaluated. The situation. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

The embodiment of No. 72-74 is a case where the surface is cut and then used after forging the various ingots, and the type of the inner layer 5, the layer structure, the thickness ratio of the surface layers 3, 4, or the B content are respectively changed and evaluated. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B content of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in the examples of Nos. 61 to 74, the neutron shielding effect was 1 or more in any of the examples, and the neutron beam shielding effect was confirmed.

[Example 4]

The neutron shielding plate 1 which is a titanium composite material having a two-layer structure according to the present invention shown in Fig. 1 is formed by melting and solidifying a single surface of a base material, and then hot rolling to form the surface layer 3 and the inside. Layer 5. Further, the neutron shielding panel 2 of the three-layer structure according to the present invention shown in FIG. 2 is borrowed. The surface layers 3, 4 and the inner layer 5 are formed by melting and solidifying the both surfaces of the base material and then hot rolling. Hereinafter, a method of manufacturing the neutron shielding plates 1 and 2 will be specifically described.

In Table 4, the intermediate-wave shielding plates 1 and 2 are shown as the examples (invention examples), and are manufactured by the following methods.

Further, the surface layer portion contains an element derived from a flat embryo (base material), but the content of the element contained in the flat embryo is only indicated in the table.

First, a titanium ingot as a material is produced by electron beam melting (EB melting), plasma arc melting (plasma melting) by a rectangular mold, or by VAR melting using a cylindrical mold.

Regarding the size of the ingot, the cylindrical ingot has a diameter of 1200 mm and a length of 2,500 mm, and the rectangular ingot has a thickness of 100 mm, a width of 1000 mm, and a length of 4,500 mm. The type is pure titanium JIS, JIS, and JIS.

The cast ingot is almost the same as the original shape, or the black skin on the surface of the ingot is cut off, and then melted and solidified. The other ingots are cut after rolling, and then melted and solidified.

The melt resolidification treatment is carried out at least on one side of the rolled surface, and is also carried out on the side in the longitudinal direction. This treatment is carried out by electron beam welding in a vacuum atmosphere of about 3 × 10 ^-3 Torr. When molten, TiB ₂ powder (100 μm or less), Ti-B alloy pellet (2 mm square, 1 mm thick), Ti -B alloy wire ( 5mm or less), Ti-B alloy film (20μm or less), Ti-B alloy mesh (will Any one of 1 mm combined into a lattice shape is added, and a molten re-solidified layer is formed into a Ti-0.1 to 3.5% B alloy to form a titanium flat embryo having a two-layer structure or a three-layer structure. For the surface layers 3 and 4 (the B-concentrated layer), the ratio of the layers of each of the total thicknesses of the titanium composite materials 1 and 2 is shown in Table 4, and the B-concentrated layer of the two surfaces in the three-layer structure. The system is adjusted to the same thickness.

When adding various materials, it is added uniformly in the whole flat embryo. In this manner, the material containing B is uniformly dispersed in the entire rolled surface of the titanium cast piece, and melted and resolidified. Further, after the melt resolidification treatment, the temperature is maintained at 100 ° C or more and less than 500 ° C for 1 hour or longer.

The melted and resolidified titanium flat embryo was heated at 800 ° C for 240 minutes using an iron steel apparatus, and then hot rolled to produce a ribbon roll having a thickness of about 4 mm. Further, the strip roll after hot rolling was subjected to a peeling film by a continuous pickling line containing nitric acid, and then visually observed the occurrence of cracking.

Further, the method for measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is a part of the hot-rolled sheet after pickling (for the front end, the center, and the rear end of the longitudinal direction, the central portion from the width direction) The material obtained by the polishing was subjected to SEM/EDS analysis, and the ratio of the surface layer 3, 4 (B concentrated layer) of the relative thickness and the B concentration of the surface layer 3, 4 (B concentrated layer) were determined. (Use the average value among the observed parts).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

Further, the evaluation of the neutron line shielding effect was carried out using Am-Be (4.5 MeV) as a line source, and a test piece of 500 mm × 500 mm × 4 mm thick was fixed at a position of 200 mm from the line source. The detector is placed at a position 300mm from the line source, and the peak of the object energy is used in the control test piece. For the measurement of the radiation equivalent, the neutron-line shielding effect is evaluated by the ratio of the radiation equivalent of the pure titanium JIS type 1 and the test piece (the sub-line shielding effect of the industrial pure titanium JIS type 1 is 1, and the value of each test piece is described) .

The results are summarized together with the test conditions in Table 4.

In the comparative examples and the examples (invention examples) shown in Nos. 75 to 83 in Table 4, the case of the original EB melted ingot after casting was used.

The comparative example of No. 75 is a case where the material containing B is not added at the time of melting and resolidification. The hot rolled sheet did not rupture, and no crack occurred in the bending test.

The comparative example of No. 76 is a case where the B concentration of the surface layers 3 and 4 exceeds 3.0%. Part of the hot rolled sheet was broken, and the cracking rate was also high in the bending test.

The comparative example of No. 77 is a case where the thickness ratio of the surface layers 3 and 4 exceeds 40%. Part of the hot rolled sheet was broken, and the cracking rate was also high in the bending test.

In the examples of No. 78 to 83 (invention example), the material containing B was changed to TiB ₂ powder, Ti-B alloy pellet, Ti-B alloy wire, Ti-B alloy film, Ti-B alloy mesh. The situation of the object evaluation. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets. No cracking occurred in the bending test.

In the examples of No. 84 to 88 (examples of the present invention), the plasma-deposited ingot after casting was used, and the material containing B was changed to TiB ₂ powder, Ti-B alloy pellet, Ti-B alloy wire, and Ti. -B alloy film, Ti-B alloy mesh for evaluation. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets. No cracking occurred in the bending test.

In the example of No. 89-93 (invention example), the black skin surface of the EB melting ingot is cut and used, and the material containing B is changed into TiB ₂ powder, Ti-B alloy pellet, Ti-B alloy, respectively. Evaluation of wire, Ti-B alloy film, Ti-B alloy mesh. Further, in the present embodiment, the side surface in the longitudinal direction is also melt-resolidified in the same manner as the rolled surface. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples of No. 94 to 98 (invention example), the black skin surface of the plasma melting ingot was cut and used, and the material containing B was changed to TiB ₂ powder, Ti-B alloy pellet, Ti-B. Evaluation of alloy wire, Ti-B alloy film, Ti-B alloy mesh. Further, in the present embodiment, the side surface in the longitudinal direction is also melt-resolidified in the same manner as the rolled surface. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Examples (No. 99 to 101) of the present invention are those in which various ingots are rolled and then the surface is cut and reused, and when molten and resolidified, TiB ₂ powder is used as the B-containing material. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Examples (No. 102 to 104) of the present invention are those in which various ingots are forged and then the surface is cut and reused, and when molten and resolidified, TiB ₂ powder is used as the B-containing material. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in the alloy of the inner layer 5 in the example of the present invention, when the tensile test was carried out on a JIS13B test piece having a thickness of 1.5 mm, the 0.2% proof stress was found to be 1000 MPa or less.

Further, in the examples (in the present invention) of Nos. 78 to 104, the neutron shielding effect was 1 or more, and the neutron beam shielding effect was confirmed. Further, a 0.5% by mass stainless steel plate (4 mm thick) was added to the amount of B used in the nuclear fuel storage rack, and the sub-shading effect was 23.7. In the examples of No. 86, 93, 106, and 108, the stainless steel was obtained. The board has a higher mid-line shielding effect.

[Example 5]

In Table 5, the intermediate-wave shielding plates 1 and 2 are shown as the respective examples (examples of the present invention) by the following methods.

Further, the surface layer portion contains an element derived from a flat embryo (base material), but the content of the element contained in the flat embryo is only indicated in the table.

According to the same procedure as in Example 4, the titanium flat embryo which had been subjected to melt resolidification was heated at 800 ° C for 240 minutes using an iron steel apparatus, and then hot rolled to obtain a ribbon roll having a thickness of about 20 mm. Further, the strip roll after hot rolling was subjected to a peeling film by a continuous pickling line containing nitric acid, and then visually observed the occurrence of cracking.

Further, the method for measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is a part of the hot-rolled sheet after pickling (for the front end, the center, and the rear end of the longitudinal direction, the central portion from the width direction) The SEM/EDS analysis was carried out by the SEM/EDS analysis, and the ratio of the surface layer 3, 4 (B concentrated layer) of the relative thickness and the B concentration of the surface layer 3, 4 (B concentrated layer) were determined. (Use the average value among the observed parts).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

Further, in the evaluation of the neutron line shielding effect, Am-Be (4.5 MeV) was used as the line source, and a test piece of 500 mm × 500 mm × 20 mm thick was fixed at a position of 200 mm from the line source. The detector is placed at a position of 300 mm from the line source, and the radiation equivalent is measured for the industrial pure titanium JIS type 1 and the test piece of the control test piece according to the peak value of the object energy. The ratio of the values was used to evaluate the neutron line shielding effect (the sub-line shielding effect of the industrial pure titanium JIS 1 type is 1 and the value of each test piece is described).

The results are summarized in Table 5 together with the test conditions.

In the comparative examples and the examples (inventive examples) shown in Nos. 105 to 112 of Table 5, the case of the original EB melted ingot after casting was used.

The comparative example of No. 105 is a case where the material containing B is not added at the time of melting and resolidification. No cracking occurred in the hot rolled sheet, and no crack occurred in the bending test.

The comparative example of No. 106 is a case where the B concentration of the surface layers 3 and 4 exceeds 3.0%. Part of the hot rolled sheet was broken, and the incidence of cracking was also high in the bending test.

The comparative example of No. 107 is a case where the thickness ratio of the surface layers 3 and 4 exceeds 40%. Part of the hot rolled sheet was broken, and the incidence of cracking was also high in the bending test.

In the examples of No. 108 to 112 (invention example), the material containing B was changed into TiB ₂ powder, Ti-B alloy pellet, Ti-B alloy wire, Ti-B alloy film, and Ti-B alloy mesh. Situation as assessed by matter. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets. No cracking occurred in the bending test.

In the examples of No. 113 to 117 (inventive example), the plasma-deposited ingot after casting was used, and the material containing B was changed to TiB ₂ powder, Ti-B alloy pellet, Ti-B alloy wire, Ti-, respectively. B alloy film, Ti-B alloy mesh and evaluated. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets. No cracking occurred in the bending test.

Examples of Nos. 118 and 119 (inventive examples) are those in which the surface of the black skin of the EB melting ingot or the plasma melting ingot is cut and used, and in the case of melting and resolidification, the TiB ₂ powder is used as the material containing B. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

In the examples (in the present invention) of No. 120 to 122, the various ingots were rolled and then the surface was cut off and used, and in the case of melting and resolidification, TiB ₂ powder was used as the B-containing material. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

After the Example No.123 ~ 125 (present invention), ingots based various forging, cutting off its surface reused, while the molten resolidification, B-containing _powder material usage of TiB. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the hot rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in the examples (No. 108 to 125) of the examples No. 108 to 125, the sub-shading effect is 1 or more in any of the examples, and the neutron line shielding can be confirmed. effect.

[Example 6]

In Table 6, the intermediate-wave shielding plates 1 and 2 are shown as the respective examples (examples of the present invention) by the following methods.

Further, the surface layer portion contains an element derived from a flat embryo (base material), but the content of the element contained in the flat embryo is only indicated in the table.

The titanium flat embryo which had been melt-resolidified in the same manner as in Example 4 was heated at 800 ° C for 240 minutes using an iron steel apparatus, and then hot rolled to produce a tape roll having a thickness of about 5 mm. Further, the strip roll after hot rolling is passed through a peeling film by a continuous pickling line containing nitric acid. Then, cold rolling was performed to form a titanium plate having a thickness of 1 mm, and as an annealing treatment, heat treatment was carried out by heating to 600 to 750 ° C in a vacuum or an inert gas atmosphere for 240 minutes. The cold-rolled sheet was visually observed for the occurrence of cracking in the surface inspection step after annealing. Further, the method of measuring the depth of the surface layers 3 and 4 (the B-concentrated layer) is to cut one part of the cold-rolled sheet (for the three portions of the front end, the center, and the rear end in the longitudinal direction, respectively, taken from the center portion in the width direction). The SEM/EDS analysis of the obtained material was carried out to obtain the ratio of the surface layer 3, 4 (B concentrated layer) of the relative thickness and the B concentration of the surface layer 3, 4 (B concentrated layer) (using the observed portion) The average value among them).

Further, in the longitudinal direction, the center, the center, and the rear end, a total of 20 bending test pieces in the L direction were taken from the center portion in the width direction, and a bending test was performed in accordance with JIS Z 2248 (Metal Material Bending Test Method). The test temperature was room temperature, and the bending test was performed by a three-point bending test at a bending angle of up to 120 degrees, and the occurrence of cracking was evaluated to determine the incidence of cracking.

In addition, the neutron line shielding effect is evaluated as a line source using Am-Be (4.5 MeV) and fixed at a position of 200 mm from the line source. 500 mm × 500 mm × 1 mm thick test piece. The detector is placed at a position of 300 mm from the line source, and the peak of the object energy is measured by the industrial pure titanium JIS type 1 (1 mm thick) and the test piece (1 mm thick) of the control test piece, respectively, from the ratio of the radiation equivalent, The neutron line shielding effect was evaluated (the sub-line shielding effect of industrial pure titanium JIS 1 is 1 and the value of each test piece is described).

The results are summarized in Table 6 together with the test conditions.

In Comparative Example and Example (Invention Example) shown in No. 126 to 131 in Table 6, the case of the original EB melted ingot after casting was used.

The comparative example of No. 126 is a case where the material containing B is not added at the time of melting and resolidification. No cracking occurred in the cold rolled sheet, and no crack occurred in the bending test.

The comparative example of No. 127 is a case where the B concentration of the surface layers 3 and 4 exceeds 3.0%. Part of the cold-rolled sheet broke, and the cracking rate was also high in the bending test.

The comparative example of No. 128 is a case where the thickness ratio of the surface layers 3 and 4 exceeds 40%. Part of the cold-rolled sheet broke, and the cracking rate was also high in the bending test.

Examples (No. 129-131) of the present invention were evaluated by changing the material containing B into TiB ₂ powder, Ti-B alloy pellet, and Ti-B alloy wire. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets. No cracking occurred in the bending test.

In the examples of No. 132-134 (invention example), the slurry-containing ingot after casting was used, and the material containing B was changed to TiB ₂ powder, Ti-B alloy film, and Ti-B alloy mesh, respectively. The situation of the assessment. In any case, the thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets. No cracking occurred in the bending test.

Examples of No. 135 and 136 (examples of the present invention) are those in which the surface of the black skin of the EB melting ingot or the plasma melting ingot is cut and used, and in the case of melting and resolidification, the TiB ₂ powder is used as the material containing B. . The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

Examples (No. 137 to 139) of the present invention are those in which various ingots are rolled and then the surface thereof is cut and reused, and when molten and resolidified, TiB ₂ powder is used as the B-containing material. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

Examples (No. 140 to 142) of the present invention are those in which various ingots are forged, and the surface thereof is cut and reused, and when molten and resolidified, TiB ₂ powder is used as the B-containing material. The thickness ratio of the surface layers 3 and 4 is in the range of 5 to 40%, and the B concentration of the surface layers 3 and 4 is in the range of 0.1 to 3.0%, so that no crack occurs in any of the cold rolled sheets, and the bending test is also performed. No cracking occurred.

Further, in any of the examples (invention examples) of Nos. 129 to 142, the neutron shielding effect was 1 or more, and the neutron beam shielding effect was confirmed.

1‧‧‧Titanium composite

3‧‧‧ surface layer

5‧‧‧ inner layer

Claims (7)

A titanium composite material comprising: an inner layer containing industrial pure titanium or a titanium alloy; and a surface layer formed on a rolled surface of at least one of the inner layers, having a chemical composition different from the inner layer; and an intermediate layer Forming between the inner layer and the surface layer, having a chemical composition different from the inner layer; and the surface layer has a thickness of 2 μm or more, and the ratio of the total thickness is 40% or less per one-sided layer; The chemical composition of the surface layer portion is, in mass%, B: 0.1 to 3.0%, and the balance: titanium and impurities; and the thickness of the intermediate layer is 0.5 μm or more. The titanium composite material according to claim 1, wherein the surface layer other than the rolled surface of the inner layer is formed with another surface layer; and the other surface layer has the same chemical composition as the surface layer. A titanium material for hot rolling, comprising: a base material containing industrial pure titanium or a titanium alloy; a surface layer joined to at least one of the rolled surfaces of the base material; and a welded portion joining the base material and the foregoing The surface layer is surrounded; and the surface layer has a chemical composition different from the above-mentioned base material, and is, by mass%: B: 0.1 to 3.0%, and the rest: titanium and impurities; The welded portion blocks the interface between the base material and the surface layer from the outside air. The titanium material for hot rolling according to the third aspect of the invention, wherein the surface layer other than the rolled surface of the base material is joined to another surface layer; and the other surface layer material has the same chemical composition as the surface layer. A titanium material for hot rolling according to claim 3 or 4, wherein the base material comprises a direct cast flat embryo. The titanium material for hot rolling according to claim 5, wherein the directly cast flat embryo has at least a part of a surface thereof formed with a molten resolidified layer. The titanium material for hot rolling according to claim 6, wherein the chemical composition of the molten resolidified layer is different from the chemical composition of the central portion of the thickness of the directly cast flat embryo.