TW201910528A - Titanium block, manufacturing method thereof, and flat titanium blank for manufacturing titanium blocks at low cost - Google Patents

Titanium block, manufacturing method thereof, and flat titanium blank for manufacturing titanium blocks at low cost Download PDF

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TW201910528A
TW201910528A TW106126534A TW106126534A TW201910528A TW 201910528 A TW201910528 A TW 201910528A TW 106126534 A TW106126534 A TW 106126534A TW 106126534 A TW106126534 A TW 106126534A TW 201910528 A TW201910528 A TW 201910528A
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Taiwan
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titanium
block
less
thickness
agglomerate
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TW106126534A
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Chinese (zh)
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藤井秀樹
白井善久
北浦知之
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日商新日鐵住金股份有限公司
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Priority to TW106126534A priority Critical patent/TW201910528A/en
Publication of TW201910528A publication Critical patent/TW201910528A/en

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Abstract

Disclosed is a titanium block, which is a plate-shaped titanium block with a thickness of 7 to 80 mm, and includes the following chemical components in percentage by mass: 0.01% to 0.5% of O, 0.01% to 5% of Fe, 0% to 8% of Al, 0% to 5% of Sn, 0% to 12% of Zr, 0% to 15% of Mo, 0% to 2% of Ta, 0% to 22% of V, 0% to 2% of Nb, 0% to 1% of Si, 0% to 10% of Cr, 0% to 0.1% of Cu, 0% to 1% of Co, 0% to 1% of Ni, 0% to 0.5% of platinum group elements, 0% to 0.2% of REM, 0% to 3% of B, 0% to 0.2% of N, 0% to 2% of C, 0% to 0.013% of H, and the balance of titanium and impurities, wherein a difference <DELTA>C between the maximum value CMAX and the minimum value CMIN of the measured value of each element is less than 0.2 CMIN or less than 0.04%, and a metal structure has a circle equivalent average crystal grain size, which is less than 10 mm and equal to or less than half the thickness, in a central portion along a thickness direction of the titanium block. The titanium block may be manufactured at low cost.

Description

鈦塊及其製造方法、以及鈦扁胚Titanium block and its manufacturing method, and titanium flat embryo

[0001] 本發明係關於鈦塊及其製造方法、以及鈦扁胚。[0001] The present invention relates to a titanium block, a method of producing the same, and a titanium flat embryo.

[0002] 鈦材為耐蝕性優良的金屬材料，故利用於使用海水之熱交換器或各種化學工廠等。又，鈦材密度較碳鋼小，比強度(每單位重量之強度)優良，故亦多使用於航空機之機體。又，藉由於汽車等之陸上輸送機器上使用鈦材，機器本身會成為輕量，因此期待油耗降低。 　　[0003] 但是，鈦材係以相較於鋼材而言，為複雜且非常多之步驟所製造。代表性的步驟係有如以下者。 　　[0004] (a)熔煉步驟：將原料之氧化鈦予以氯化而成為四氯化鈦後，以鎂或鈉還原，藉以製造塊狀且海綿狀之金屬鈦(以下稱為「海綿鈦」)的步驟。 　　[0005] (b)熔解步驟：將海綿鈦壓製成形而成為電極，於真空電弧熔解爐熔解而製造鑄塊之步驟。 　　[0006] (c)鍛造步驟：將鑄塊熱鍛造而製造扁胚(slab)(熱壓延素材)或胚料(billet)(熱擠壓或熱壓延等之素材)等的步驟。 　　[0007] (d)熱加工步驟：將扁胚或胚料加熱，予以熱壓延或擠壓加工，以製造板或圓棒等的步驟。 　　[0008] (e)冷加工步驟：將板或圓棒進一步予以冷壓延加工而製造薄板或圓棒、線等的步驟。 　　[0009] 如此地，由於鈦材係藉由許多步驟而製造，故價格非常高。因此，鈦材幾乎未被應用於汽車等之陸上輸送機器。為了促進鈦材的利用，有必要提高其製造製程之生產性。作為對應該課題之技術，係採取省略鈦材之製造步驟的措施。 　　[0010] VAR(真空電弧熔解)，僅可製造圓柱形狀之鈦鑄塊，因此為了於之後進行熱壓延使成為薄板，必須將圓柱狀之鈦鑄塊熱鍛造，而成為長方體形狀之鈦，亦即鈦扁胚。 　　[0011] 另一方面，於電子束熔解或電漿熔解中，係將熔解之鈦保持於容器(冷爐床)後注入各種形狀之模具中。因此，藉由使用長方體之模具，可直接得到扁胚形狀之鈦鑄塊，可省略鍛造步驟(直接扁胚鑄造方法)。所熔解之鈦，係由與模具接觸的鈦鑄塊表層起開始凝固，最後厚度中心部凝固而得到鈦鑄塊。同時，鈦鑄塊係由上方向下方提拉，由下方向上方慢慢凝固。 　　[0012] 專利文獻1中，揭示省略熔解步驟而製造鈦鑄塊之發明。該鈦鑄塊(扁胚)，係藉由將多孔質鈦(海綿鈦)壓縮成形為鑄塊狀，且將其表面於真空下熔解而製造，內部為多孔質鈦，而且其全表面係由稠密的鈦所被覆。依專利文獻1所揭示之發明，係使用海綿鈦或其壓縮成形體來製造扁胚形狀之鈦鑄塊，因此可製作薄的扁胚。 　　[0013] 專利文獻2中，揭示對鈦合金粉添加銅粉、鉻粉或鐵粉，封入碳鋼製之套包(capsule)中，加熱並熱擠壓而製造鈦合金圓棒的發明。專利文獻3中，揭示將含氫之鈦粉末或鈦合金粉末填充於套包中，藉由減壓同時加熱而脫氫後，熱擠壓以製造鈦圓棒或鈦合金圓棒的發明。專利文獻4中，揭示關於對以純鈦材所形成之捆包材料，填充由海綿鈦、鈦團塊(titanium briquette)及鈦殘屑(titanium scrap)中選擇的一種以上而得之鈦材的發明。 [先前技術文獻] [專利文獻] 　　[0014] 　　[專利文獻1]日本特開2015-45040號公報 　　[專利文獻2]日本特開2014-019945號公報 　　[專利文獻3]日本特開2012-041583號公報 　　[專利文獻4]國際公開第2016/056607號[0002] Since a titanium material is a metal material excellent in corrosion resistance, it is used in a heat exchanger using sea water or various chemical factories. Moreover, the density of titanium is smaller than that of carbon steel, and the specific strength (strength per unit weight) is excellent, so it is also used in the body of an aircraft. Moreover, since the titanium material is used on a land transportation machine such as an automobile, the machine itself becomes lightweight, and therefore fuel consumption is expected to decrease. [0003] However, titanium is produced in a complicated and very numerous step compared to steel. Representative steps are as follows. [0004] (a) Smelting step: chlorination of titanium oxide as a raw material to form titanium tetrachloride, followed by reduction with magnesium or sodium, thereby producing a massive and sponge-like metal titanium (hereinafter referred to as "sponge titanium") A step of. (b) Melting step: a step of press-forming a sponge titanium into an electrode and melting it in a vacuum arc melting furnace to produce an ingot. (c) Forging step: a step of hot forging an ingot to produce a slab (hot rolled material) or a billet (material for hot extrusion or hot rolling). (d) Thermal processing step: a step of heating a flat blank or an aggregate to be subjected to hot calendering or extrusion processing to produce a plate or a round bar or the like. (e) Cold working step: a step of further subjecting a plate or a round bar to cold rolling to produce a thin plate or a round bar, a wire or the like. As such, since the titanium material is manufactured by many steps, the price is very high. Therefore, titanium material is hardly applied to land transportation machines such as automobiles. In order to promote the utilization of titanium materials, it is necessary to improve the productivity of the manufacturing process. As a technique corresponding to the problem, measures for omitting the manufacturing steps of the titanium material are adopted. [0010] VAR (vacuum arc melting), only a cylindrical ingot can be produced in a cylindrical shape. Therefore, in order to form a thin plate after hot rolling, it is necessary to thermally forge a cylindrical titanium ingot to form a rectangular parallelepiped titanium. That is, titanium flat embryo. [0011] On the other hand, in electron beam melting or plasma melting, the melted titanium is held in a container (cold hearth) and injected into a mold of various shapes. Therefore, by using a rectangular parallelepiped mold, a flat ingot-shaped titanium ingot can be directly obtained, and the forging step (direct flat embryo casting method) can be omitted. The molten titanium is solidified by the surface of the titanium ingot which is in contact with the mold, and finally the central portion of the thickness is solidified to obtain a titanium ingot. At the same time, the titanium ingot is pulled from the top to the bottom and slowly solidifies from the bottom to the top. [0012] Patent Document 1 discloses an invention in which a titanium ingot is produced by omitting a melting step. The titanium ingot (flat embryo) is produced by compression-molding porous titanium (sponge titanium) into an ingot shape and melting the surface thereof under vacuum, and the inside is porous titanium, and the entire surface thereof is composed of Covered with dense titanium. According to the invention disclosed in Patent Document 1, a titanium ingot having a flat embryo shape is produced by using titanium sponge or a compression molded body thereof, so that a thin flat embryo can be produced. [0013] Patent Document 2 discloses an invention in which a copper alloy powder, a chromium powder, or an iron powder is added to a titanium alloy powder, sealed in a carbon steel capsule, and heated and hot pressed to produce a titanium alloy round rod. Patent Document 3 discloses an invention in which a hydrogen-containing titanium powder or a titanium alloy powder is filled in a package, dehydrogenated by heating under reduced pressure, and then hot-extruded to produce a titanium round bar or a titanium alloy round bar. Patent Document 4 discloses an invention of a titanium material obtained by filling one or more selected from a sponge titanium, a titanium briquette, and a titanium scrap to a packing material formed of a pure titanium material. . [Prior Art Document] [Patent Document 1] [Patent Document 1] Japanese Laid-Open Patent Publication No. JP-A No. Hei. No. Hei. No. Hei. Bulletin [Patent Document 4] International Publication No. 2016/056607

[發明所欲解決之課題] 　　[0015] 直接扁胚鑄造方法，雖為可省略鍛造步驟之優良方法，但所得到之扁胚厚度為100mm以上，通常為200mm至400mm左右。由於扁胚之厚度係以模具之厚度決定，故若使模具之厚度為薄，則可使扁胚之厚度為薄。 　　[0016] 但是，模具之厚度較100mm更薄時，將熔融鈦由冷爐床注入於模具時，會產生熔融鈦飛散於模具外，或熔融鈦不會均等地由注入之部分朝向模具之寬度方向流入的不良狀況。 　　[0017] 又，為了由100mm以上厚度的扁胚得到厚度數mm以下的鈦薄板，由於必須實施大的加工，故必須要巨大的熱加工設備，或必須實施多次重複熱加工，其係效率不佳的。 　　[0018] 進一步地，100mm以上厚度的扁胚，由於其厚度，因而內部的冷卻速度慢，結晶粒會成長為非常大。因此，為了得到製品所必要的拉伸特性等之機械特性，必須實施大的加工將大型的結晶粒破壞而變細。由於其厚度，凝固偏析會增大，扁胚之表層與中心部之成分的差距大。又，於鈦鑄塊之長度(上下)方向，最後所凝固之扁胚上方的厚度中心部，特別容易凝固偏析，容易正偏析之Fe、Cr、Co、Cu、Ni、V、Si等會變濃。 　　[0019] 直接扁胚鑄造方法，係將於真空腔室內熔解之鈦保持於冷爐床，因此鈦或副原料(合金添加元素)之一部分會揮發而大量附著於腔室壁面。因此，得到鑄塊時的良率會變差。又，附著於腔室壁面之揮發物的去除作業需要時間，因此作業性不佳。為含有較鈦更易揮發之元素(Al、Cu、Sn等)的鈦合金的情況時，容易揮發之元素於扁胚中的含量會較於鈦原料中的含量減少。因此，係進行預測各元素之揮發量，將對應該等之量較多地添加於鈦原料中。 　　[0020] 但是，該揮發量係隨著熔解速度或扁胚之提拉速度、EB照射條件等之操作條件而大幅變化。例如，熔解速度係隨著鈦原料之大小或形狀而變動，熔解速度降低時，流過冷爐床之熔融鈦量會減少，揮發量增加。於冷爐床內之熔融鈦變少的鑄造初期及末期，扁胚之提拉速度會降低。其間，對模具內之熔融鈦照射EB之時間變長，揮發量增加。又，照射條件基本上可為一定，但發生操作事故時，必須降低輸出或停止，因此熔解速度會下降，或熔解停止。輸出降低時，揮發量會減少。預測並管理此等操作條件極為困難，因此，於扁胚的長度方向無法避免成分的變動。 　　[0021] 專利文獻1所揭示之鈦鑄塊的內部係粒狀之海綿鈦，因此基本上僅可得到與海綿鈦相同化學組成之鈦鑄塊。欲得到與海綿鈦之化學組成不同化學組成的鈦鑄塊，必須添加必要之元素。例如，為了提高強度而欲增加鈦之氧時係於海綿鈦中添加氧化鈦粉末，欲成為Ti-6Al-4V合金時，係於海綿鈦中添加Al-V合金粒或Al粒，並進行混合。 　　[0022] 但是，由於之後並無熔解步驟，故海綿鈦與添加元素粉末或粒子不容易成為均質。欲於熱加工後進行固溶化熱處理而藉由各元素之擴散謀求均質化，必須進行大量時間之固溶化處理，並不實用。因此，專利文獻1所揭示之發明中，僅可製造具有與海綿鈦同等化學組成之鈦鑄塊，無法製造鈦合金鑄塊。 　　[0023] 進一步地，將鑄造之表面直接予以熱壓延時，於所得之鈦薄板表面容易產生疤狀之表面缺陷。專利文獻1揭示之鈦鑄塊，係僅將其表面熔解、凝固者，因此其表面成為粗的鑄造組織(大型的結晶粒)。其係因於下個步驟之熱壓延時，鑄塊表層之大型的鑄造組織(大型的結晶粒)，因結晶方位之差異所致之強的塑性各向異性，於鑄塊表面產生起伏而成為疤狀之表面缺陷之故。 　　[0024] 依照專利文獻2、3揭示之發明，原料可使用粉末且各種元素亦以粉末的形態添加，來製造各種之鈦或鈦合金的圓棒。此係因使用較海綿鈦更細的粉末，故熱加工後之固溶化處理即使為較短時間亦可得到均質的圓棒。但是，為了製造鈦粉末或鈦合金粉末、合金添加用粉末等之原料粉末，需要勞力與成本。 　　[0025] 依照專利文獻4揭示之發明，因為可省略熔解步驟及鍛造步驟，故可價格便宜地得到鈦材。但是，由於直接使用海綿鈦等，故與專利文獻1之發明同樣地，會產生僅可製造具有與海綿鈦同等之化學組成的鈦鑄塊，且無法製造鈦合金鑄塊之問題。 　　[0026] 本發明係有鑑於如此實情，其目的為以低成本來製造作為鈦薄板或鈦線材之素材的熱加工用或冷加工用之鈦塊，特別是厚度薄或小直徑之具有各種化學組成的鈦塊。 [用以解決課題之手段] 　　[0027] 本發明者等人為了解決上述課題而重複努力探討的結果，思及可製造可省略鍛造步驟，進而可使熱加工步驟簡化之鈦塊。 　　[0028] 圖1為示意性顯示鈦團塊1之說明圖。 　　[0029] 所使用之原料，為以通常之步驟所製造的能夠以較便宜的價格獲得之海綿鈦1a。直接以粒狀之海綿鈦1a進行電子束熔解，形狀亦不會整齊，故如圖1所示，係將海綿鈦1a壓縮成形而成為長方體形狀之鈦團塊1。 　　[0030] 此時、係將含有為了得到必要化學組成之鈦塊所必要的元素(氧、Fe、Al、V等)之副原料1c添加於海綿鈦1a並混合後，壓縮成形而得到鈦團塊1。 　　[0031] 鈦團塊1係於內部存在有空隙1d，因此於減壓下將存在於空隙1d之空氣去除後，藉由電子束將鈦團塊1之厚度方向的一部分(例如大約一半)2a熔解。 　　[0032] 圖2為示意性顯示鈦塊2之說明圖。 　　[0033] 之後，將鈦團塊1反轉，將尚未熔解之厚度方向之剩餘一部分(例如大約一半)2b同樣地藉由電子束熔解。本發明者等人，發現藉由空隙1d之抽真空及鈦團塊1之熔解，所添加之副原料1c會與海綿鈦1a一起熔解而成為均質，如圖2所示般可得到厚度薄之鈦塊2。 　　[0034] 此時，欲使鈦塊2之內部不殘存氣泡，必須充分去除海綿鈦1a粒間之空隙1d中所存在的空氣，本發明者等人亦發現，為了達成上述者，將電子束熔解前之鈦團塊1置於極力減壓之環境係重要的。 　　[0035] 本發明者等人亦發現，由於藉由電子束而使鈦團塊1之一部分熔解而凝固，又，因鈦塊2之厚度薄，故相較於如以往之熔解步驟般將原料全部熔解後注入模具進行凝固及冷卻之厚度大的鈦材而言，凝固後之冷卻速度快，鈦塊2之內部結晶粒不會大型化。 　　[0036] 又，亦發現藉由將海綿鈦1a壓縮成形為圓柱狀、稜柱狀或多稜柱狀之棒形狀而成為鈦團塊1，同樣地進行電子束熔解，可得到圓柱狀、稜柱狀或多稜柱狀之棒形狀的小直徑之鈦塊2。 　　[0037] 圖4為示意性顯示鈦扁胚3之說明圖。 　　[0038] 進一步地，本發明者等人亦發現，為了抑制熱加工時之表面缺陷，係將上述得到之鈦塊2，填充於以具有同種化學組成之鈦板材4a所製作之容器(捆包材料)4中，將捆包材料4之連接部全部熔接而形成熔接部5，得到圖4所示之鈦扁胚3。該鈦扁胚3，可使用作為熱加工用鈦素材。 　　[0039] 本發明係基於此等新穎見解者，如以下列記所述。 　　[0040] (1)一種鈦塊，其係厚度為7~80mm之板狀之鈦塊， 　　其化學組成，以質量%計，為 　　O：0.01~0.5%、 　　Fe：0.01~5%、 　　Al：0~8%、 　　Sn：0~5%、 　　Zr：0~12%、 　　Mo：0~15%、 　　Ta：0~2%、 　　V：0~22%、 　　Nb：0~2%、 　　Si：0~1%、 　　Cr：0~10%、 　　Cu：0~0.1%、 　　Co：0~1%、 　　Ni：0~1%、 　　鉑族元素：0~0.5%、 　　REM：0~0.2%、 　　B：0~3%、 　　N：0~0.2%、 　　C：0~2%、 　　H：0~0.013%， 　　剩餘部分為鈦及雜質， 　　各元素之測定值的最大值CMAX 與最小值CMIN 之差分⊿C，為未達0.2CMIN 或未達0.04%， 　　金屬組織，為 　　前述鈦塊於厚度方向之中央部的圓當量平均結晶粒徑為10mm以下、且為前述鈦塊之厚度的一半以下。 　　[0041] (2)一種鈦塊，其係具有垂直於長度方向之截面為直徑10~80mm之圓形的圓柱形狀，或圓當量直徑為10~80mm之五角形以上的多角形之柱形狀的鈦塊， 　　其化學組成，以質量%計，為 　　O：0.01~0.5%、 　　Fe：0.01~5%、 　　Al：0~8%、 　　Sn：0~5%、 　　Zr：0~12%、 　　Mo：0~15%、 　　Ta：0~2%、 　　V：0~22%、 　　Nb：0~2%、 　　Si：0~1%、 　　Cr：0~10%、 　　Cu：0~0.1%、 　　Co：0~1%、 　　Ni：0~1%、 　　鉑族元素：0~0.5%、 　　REM：0~0.2%、 　　B：0~3%、 　　N：0~0.2%、 　　C：0~2%、 　　H：0~0.013%、 　　剩餘部分為鈦及雜質， 　　各元素之測定值的最大值CMAX 與最小值CMIN 之差分⊿C，為未達0.2CMIN 或未達0.04%， 　　金屬組織，為 　　於垂直於前述鈦塊之長度方向的截面，具有於由表面朝向中心之方向延伸的柱狀組織，前述截面之中心位置的圓當量平均結晶粒徑為10mm以下，且為前述截面之直徑的一半以下。 　　[0042] (3)一種鈦扁胚，其具備具有與如上述(1)或(2)之鈦塊同種之化學組成的捆包材料，與 　　填充於前述捆包材料之內部的如上述(1)或(2)之鈦塊，且 　　前述捆包材料之內壓為10Pa以下。 　　[0043] (4)如上述(1)或(2)之鈦塊之製造方法，其具備 　　將由海綿鈦及鈦殘屑中選擇之一種以上，與含有為了調整化學組成所必要之元素的副原料予以壓縮成形而得到鈦團塊之壓縮成形步驟、 　　於1Pa以下之減壓下對前述鈦團塊之表面照射電子束以將前述鈦團塊之全部熔解而成為鈦塊之熔解步驟。 　　[0044] (5)如上述(4)之鈦塊之製造方法，其中前述熔解步驟，具備對前述鈦團塊之任意表面照射電子束，由其表面起熔解厚度方向之一部分之步驟，及對任意之其他表面照射電子束，至少將未熔解之鈦團塊熔解之步驟。 [發明之效果] 　　[0045] 依照本發明，能夠以低成本來製造具有各種化學組成之鈦塊，其係可使用於以熱加工或冷加工來製造鈦薄板或鈦線材的素材。 　　本發明之鈦塊，為厚度薄或小直徑之扁胚(四稜柱(例如板狀)、圓柱、多稜柱)，由於製造鈦薄板或棒時的加工率少即可，故可效率良好且價格便宜地製造鈦薄板或棒。 　　本發明之鈦塊，由於為厚度薄之板狀或小直徑的柱狀鈦塊，故厚的中心部(板狀之鈦塊)或垂直於長度方向之截面的中心部(柱狀之鈦塊)的結晶粒小，凝固偏析小。 　　將本發明之鈦塊填充於由鈦板材所構成的捆包材料而得之鈦扁胚，可抑制熱加工時之表面缺陷產生。 　　依照本發明之製造方法，僅將電子束之照射條件調整為一定，即可穩定地得到目標成分之鈦鑄塊。[Problems to be Solved by the Invention] The direct slab casting method is an excellent method in which the forging step can be omitted, but the obtained spheroid thickness is 100 mm or more, and usually about 200 mm to 400 mm. Since the thickness of the flat embryo is determined by the thickness of the mold, if the thickness of the mold is made thin, the thickness of the flat embryo can be made thin. [0016] However, when the thickness of the mold is thinner than 100 mm, when molten titanium is injected into the mold from the cold hearth, molten titanium is scattered outside the mold, or the molten titanium is not uniformly distributed from the injected portion toward the width of the mold. Bad condition of inflow. [0017] Further, in order to obtain a titanium thin plate having a thickness of several mm or less from a flat embryo having a thickness of 100 mm or more, since it is necessary to carry out large processing, it is necessary to have a large thermal processing apparatus, or it is necessary to perform repeated hot working, which is efficient. Not good. [0018] Further, the flat embryo having a thickness of 100 mm or more, due to its thickness, has a slow internal cooling rate, and the crystal grains grow to be very large. Therefore, in order to obtain the mechanical properties such as the tensile properties necessary for the product, it is necessary to perform a large processing to break and reduce the large crystal grains. Due to its thickness, solidification segregation increases, and the difference between the surface layer of the flat embryo and the center portion is large. Moreover, in the length (upper and lower) direction of the titanium ingot, the center portion of the thickness above the finally solidified flat embryo is particularly prone to solidification segregation, and Fe, Cr, Co, Cu, Ni, V, Si, etc. which are prone to segregation are likely to change. concentrated. [0019] The direct slab casting method is to keep the titanium melted in the vacuum chamber in the cold hearth, so that part of the titanium or the auxiliary material (alloy additive element) volatilizes and adheres to the wall surface of the chamber in a large amount. Therefore, the yield at the time of obtaining an ingot is deteriorated. Moreover, the removal operation of the volatile matter adhering to the wall surface of the chamber takes time, so workability is poor. In the case of a titanium alloy containing an element more volatile than titanium (Al, Cu, Sn, etc.), the content of the element which is easily volatilized in the spheroid is reduced as compared with the content in the titanium material. Therefore, the amount of volatilization of each element is predicted, and a corresponding amount is added to the titanium raw material in a large amount. [0020] However, the amount of volatilization greatly changes depending on the melting conditions, the pulling speed of the flat embryo, and the operating conditions such as the EB irradiation conditions. For example, the melting rate varies depending on the size or shape of the titanium raw material, and when the melting rate is lowered, the amount of molten titanium flowing through the cold hearth is reduced, and the amount of volatilization is increased. In the initial stage and the end stage of casting in which the molten titanium in the cold hearth is reduced, the pulling speed of the flat embryo is lowered. In the meantime, the time during which the molten titanium in the mold is irradiated with EB becomes longer, and the amount of volatilization increases. Further, the irradiation condition can be substantially constant, but when an operation accident occurs, the output must be lowered or stopped, so that the melting speed is lowered or the melting is stopped. When the output is lowered, the amount of volatilization is reduced. It is extremely difficult to predict and manage such operating conditions, and therefore variations in composition cannot be avoided in the longitudinal direction of the slab. [0021] The inside of the titanium ingot disclosed in Patent Document 1 is a granular titanium sponge, and thus substantially only a titanium ingot having the same chemical composition as that of titanium sponge is obtained. In order to obtain a titanium ingot having a chemical composition different from that of titanium sponge, it is necessary to add necessary elements. For example, in order to increase the strength, in order to increase the oxygen of titanium, titanium oxide powder is added to the titanium sponge, and when it is to be a Ti-6Al-4V alloy, Al-V alloy particles or Al particles are added to the titanium sponge and mixed. . [0022] However, since there is no melting step thereafter, the titanium sponge and the additive element powder or particles are not easily homogenized. It is necessary to perform a solution heat treatment after hot working and to homogenize by diffusion of each element, and it is necessary to carry out a solid solution treatment for a large amount of time, which is not practical. Therefore, in the invention disclosed in Patent Document 1, only a titanium ingot having the same chemical composition as that of titanium sponge can be produced, and a titanium alloy ingot cannot be produced. [0023] Further, the surface to be cast is directly subjected to hot pressing delay, and the surface of the obtained titanium thin plate is liable to cause a flawed surface defect. The titanium ingot disclosed in Patent Document 1 is obtained by melting and solidifying only the surface thereof, so that the surface thereof becomes a coarse cast structure (large crystal grains). Due to the hot pressing delay of the next step, the large cast structure (large crystal grains) on the surface of the ingot, due to the strong plastic anisotropy due to the difference in crystal orientation, causes undulations on the surface of the ingot. The surface defects of the braided surface. [0024] According to the invention disclosed in Patent Documents 2 and 3, a raw material can be used as a powder, and various elements are also added in the form of a powder to produce various round bars of titanium or titanium alloy. Since this is a finer powder than sponge titanium, the solution treatment after hot working can obtain a homogeneous round bar even for a short period of time. However, labor and cost are required in order to produce a raw material powder such as a titanium powder, a titanium alloy powder, or an alloy addition powder. [0025] According to the invention disclosed in Patent Document 4, since the melting step and the forging step can be omitted, the titanium material can be obtained inexpensively. However, since titanium sponge or the like is used as it is, in the same manner as the invention of Patent Document 1, there is a problem that a titanium ingot having a chemical composition equivalent to that of titanium sponge can be produced, and a titanium alloy ingot cannot be produced. The present invention has been made in view of such circumstances, and an object thereof is to manufacture a titanium block for hot working or cold working as a material of a titanium thin plate or a titanium wire at a low cost, particularly a thin or small diameter having various chemical compositions. Titanium block. [Means for Solving the Problem] The inventors of the present invention have repeatedly tried to solve the above problems, and have thought that it is possible to manufacture a titanium block which can omit the forging step and further simplify the hot working step. 1 is an explanatory view schematically showing a titanium agglomerate 1. The raw material used is sponge titanium 1a which can be obtained in a usual procedure and which can be obtained at a relatively inexpensive price. The electron beam is melted directly in the granular sponge titanium 1a, and the shape is not uniform. Therefore, as shown in Fig. 1, the titanium sponge 1a is compression-molded to form a rectangular block 1 in the shape of a rectangular parallelepiped. [0030] At this time, the auxiliary material 1c containing an element (oxygen, Fe, Al, V, etc.) necessary for obtaining a titanium block having a necessary chemical composition is added to the titanium sponge 1a and mixed, and then compression-molded to obtain a titanium group. Block 1. [0031] The titanium agglomerate 1 has a void 1d therein, and therefore, after the air existing in the void 1d is removed under reduced pressure, a part (for example, about half) of the thickness direction of the titanium agglomerate 1 is 2a by an electron beam. Melt. 2 is an explanatory view schematically showing a titanium block 2. [0033] Thereafter, the titanium agglomerate 1 is reversed, and the remaining portion (for example, about half) 2b of the thickness direction which has not been melted is similarly melted by an electron beam. The present inventors have found that by adding the vacuum of the void 1d and the melting of the titanium agglomerate 1, the added auxiliary material 1c is melted together with the titanium sponge 1a to be homogeneous, and as shown in Fig. 2, the thickness is thin. Titanium block 2. At this time, in order to prevent air bubbles from remaining inside the titanium block 2, it is necessary to sufficiently remove the air existing in the void 1d between the titanium sponges 1a, and the inventors have found that in order to achieve the above, the electron beam is used. It is important that the titanium agglomerate 1 before melting is placed in an environment where extreme decompression is performed. The present inventors have also found that since one part of the titanium agglomerate 1 is melted by the electron beam to be solidified, and since the thickness of the titanium block 2 is thin, the raw material is compared with the conventional melting step. After the titanium material which has been melted and injected into the mold for solidification and cooling, the cooling rate after solidification is fast, and the internal crystal grains of the titanium block 2 are not enlarged. [0036] Further, it has been found that the titanium agglomerate 1 is formed by compression-molding the titanium sponge 1a into a rod shape of a columnar shape, a prismatic shape, or a polygonal prism shape, and the electron beam is melted in the same manner to obtain a columnar shape, a prismatic shape, or A small diameter titanium block 2 in the shape of a rod having a polygonal prism shape. 4 is an explanatory view schematically showing a titanium flat embryo 3. Further, the inventors of the present invention have found that in order to suppress surface defects during hot working, the titanium block 2 obtained above is filled in a container made of a titanium plate 4a having the same chemical composition (bundle) In the material) 4, the joint portion of the packing material 4 is all welded to form the welded portion 5, and the titanium flat blank 3 shown in Fig. 4 is obtained. The titanium flat blank 3 can be used as a titanium material for hot working. [0039] The present invention is based on such novels as described below. [0040] (1) A titanium block which is a plate-shaped titanium block having a thickness of 7 to 80 mm, and its chemical composition, in mass%, is O: 0.01 to 0.5%, Fe: 0.01 to 5%, Al: 0~8%, Sn: 0~5%, Zr: 0~12%, Mo: 0~15%, Ta: 0~2%, V: 0~22%, Nb: 0~2%, Si:0 ~1%, Cr: 0~10%, Cu: 0~0.1%, Co: 0~1%, Ni: 0~1%, platinum group elements: 0~0.5%, REM: 0~0.2%, B: 0~3%, N:0~0.2%, C:0~2%, H:0~0.013%, the remainder is titanium and impurities, the difference between the maximum value of the measured values of each element C MAX and the minimum value C MIN ⊿C is less than 0.2 C MIN or less than 0.04%, and the metal structure is a circle-equivalent average crystal grain size of the center portion of the titanium block in the thickness direction of 10 mm or less and half or less of the thickness of the titanium block. [0041] (2) A titanium block having a circular cylindrical shape having a diameter of 10 to 80 mm in a cross section perpendicular to the longitudinal direction, or a polygonal cylindrical shape having a circular equivalent diameter of 10 to 80 mm and a polygonal shape. The chemical composition of the block, in mass%, is O: 0.01 to 0.5%, Fe: 0.01 to 5%, Al: 0 to 8%, Sn: 0 to 5%, Zr: 0 to 12%, Mo: 0 ~15%, Ta: 0~2%, V: 0~22%, Nb: 0~2%, Si: 0~1%, Cr: 0~10%, Cu: 0~0.1%, Co: 0~ 1%, Ni: 0~1%, platinum group elements: 0~0.5%, REM: 0~0.2%, B: 0~3%, N: 0~0.2%, C: 0~2%, H: 0 ~0.013%, the remainder is titanium and impurities, the difference between the maximum value of the measured value of each element C MAX and the minimum value C MIN ⊿C, which is less than 0.2 C MIN or less than 0.04%, the metal structure is perpendicular to The cross section in the longitudinal direction of the titanium block has a columnar structure extending from the surface toward the center, and the circle-equivalent average crystal grain size at the center of the cross section is 10 mm or less and is less than or equal to half the diameter of the cross section. (3) A titanium slab having a packing material having the same chemical composition as the titanium block of the above (1) or (2), and filling the inside of the packing material as described above (1) Or the titanium block of (2), and the internal pressure of the above-mentioned packing material is 10 Pa or less. (4) The method for producing a titanium block according to the above (1) or (2), which comprises one or more selected from the group consisting of sponge titanium and titanium residues, and an auxiliary material containing an element necessary for adjusting a chemical composition. A compression molding step of obtaining a titanium agglomerate by compression molding, and irradiating an electron beam on the surface of the titanium agglomerate under a reduced pressure of 1 Pa or less to melt all of the titanium agglomerate to form a titanium block melting step. (5) The method for producing a titanium block according to the above (4), wherein the melting step includes a step of irradiating an arbitrary surface of the titanium agglomerate with an electron beam, and melting a part of the thickness direction from the surface thereof, and Any other surface illuminates the electron beam, at least the step of melting the unmelted titanium agglomerate. [Effects of the Invention] According to the present invention, it is possible to manufacture a titanium block having various chemical compositions at a low cost, which can be used for producing a material of a titanium thin plate or a titanium wire by hot working or cold working. The titanium block of the present invention is a flat or thin-diameter flat embryo (a quadrangular prism (for example, a plate), a cylinder, or a polygonal prism), and the processing rate when manufacturing a titanium thin plate or a rod is small, so that the efficiency is good and the price is high. Titanium sheets or rods are inexpensively manufactured. Since the titanium block of the present invention is a plate-shaped or small-diameter columnar titanium block having a small thickness, a thick central portion (plate-shaped titanium block) or a central portion perpendicular to the longitudinal direction (columnar titanium block) The crystal grains are small and the solidification segregation is small. The titanium slab obtained by filling the titanium block of the present invention in a packing material composed of a titanium plate material can suppress the occurrence of surface defects during hot working. According to the production method of the present invention, the titanium ingot of the target component can be stably obtained only by adjusting the irradiation conditions of the electron beam to be constant.

[0047] 參照添附圖式，依次說明本發明所用之原料、鈦團塊、鈦塊、鈦扁胚。再者，以後的說明中，關於化學組成之「%」，只要無特別指明，意指「質量%」。 　　[0048] 圖1為示意性顯示鈦團塊1之說明圖，圖2為示意性顯示鈦塊2之說明圖，圖4及圖5為示意性顯示鈦扁胚3、30之說明圖。 　　[0049] 如圖1所示，鈦團塊1，係將海綿鈦1a及鈦殘屑1b之一種以上，與含有為了達成作為最終製品之功能所必要的元素(例如氧、Fe、Al、V等)之副原料1c予以混合，例如壓縮成形為長方體形狀而得到。 　　[0050] 1.鈦團塊1之原料 　　首先，說明鈦團塊1之原料。鈦團塊1之原料，含有海綿鈦1a及鈦殘屑1b之至少一方，且含有選擇性地含有各種元素之副原料1c。 　　[0051] (1-1)海綿鈦之大小 　　使用海綿鈦1a作為鈦團塊1之原料時，可使用以以往之克羅爾法(Kroll process)等之熔煉步驟所製造者。以該熔煉步驟所得到之海綿鈦1a，通常為多達數噸之大的塊狀物，因此較期望使用與以往步驟同樣地經破碎而成為粒狀者。 　　[0052] 海綿鈦1a之大小，以平均粒徑計較期望為1mm以上25mm以下(惟，使用於板狀鈦塊時，係鈦塊之厚度以下；使用於多稜柱狀或圓柱狀鈦塊時，係鈦塊之直徑以下)。平均粒徑未達1mm時，破碎需要時間，亦產生多量微細粉塵而會飛散，因此製造效率降低。另一方面，平均粒徑大於25mm時，於之後步驟照射電子束可使鈦團塊1熔解的範圍係有所限制，故有無法與副原料1c均勻熔解的可能性。 　　[0053] (1-2)海綿鈦之化學組成 　　海綿鈦1a為鈦塊2之原料，於鈦以外係含有氧、鐵、氮、碳、氫、氯、鎂等。具體而言，例示有氧0.40%以下、鐵0.50%以下、氮0.05%以下、碳0.08%以下、氫0.013%以下、氯0.10%以下、鎂0.10%以下。 　　[0054] 此等之量較期望為與對鈦塊2所要求之量同等或其以下。海綿鈦1a中所含有的鈦以外之元素的量，只要為與對鈦塊2所要求的量同等，則可直接使用海綿鈦1a。海綿鈦1a中所含有的鈦以外之元素的量若少於對鈦塊2所要求之鈦以外的元素量時，只要藉由添加其化學組成所必要量之副原料1c來補足即可。 　　[0055] 海綿鈦1a中所含有的鈦以外之元素的量若多於對鈦塊2所要求之鈦以外之元素的量，且該海綿鈦1a之量少於對鈦塊2所要求之量，則與鈦以外之元素量少的其他海綿鈦適當地混合，來稀釋鈦以外之元素。藉此，可得到目標之鈦塊2。但是，該海綿鈦1a之鈦以外之元素的量過多時，由於無法稀釋，故無法使用。 　　[0056] 接著，說明可作為原料使用之鈦殘屑1b。 　　[0057] 鈦殘屑1b，係指於鈦材製造步驟中所產生之不為製品的殘餘材，或為了使鈦素材成為製品形狀而進行切削、研削時所產生的鈦切粉；作為製品使用後之不要的鈦材等。 　　[0058] (1-3)鈦殘屑之大小 　　鈦殘屑1b之大小，與海綿鈦1a同樣地，以平均粒徑計較期望為1mm以上25mm以下(惟，使用於板狀鈦塊時係鈦塊之厚度以下，使用於多稜柱狀或圓柱狀鈦塊時係鈦塊之直徑以下)。平均粒徑未達1mm時，破碎需要時間，亦產生多量之微細粉塵而會飛散，因此製造效率降低。另一方面，平均粒徑大於25mm時，於之後步驟照射電子束可使鈦團塊1熔解的範圍係有所限制，故有無法與所添加的副原料1c均勻熔解的可能性。 　　[0059] 鈦殘屑1b，雖以其原本的狀態填充於金屬模亦可，但容積比重小的鈦切粉等，為了更有效率地，或更多量地填充，亦可預先壓縮而使容積比重增大，或與海綿鈦1a混合後來填充。 　　[0060] (1-4)鈦殘屑之化學組成 　　鈦殘屑1b，當與海綿鈦1a混合時，較佳為相當於與該海綿鈦1a同種之JIS1種、JIS2種、JIS3種或JIS4種(JIS H 4600(2012年)鈦及鈦合金-板及條)的化學組成。鈦殘屑1b，亦可為與作為鈦塊2之目標的化學組成同種。此處，同種之化學組成，具體而言，係指屬於JIS之相同規格。例如，海綿鈦1a之化學組成屬於JIS1種的情況時，則混合之鈦殘屑1b亦可為屬於JIS1種之化學組成。或者欲得到屬於JIS2種之化學組成的鈦塊2時，海綿鈦1a可為屬於JIS1種之化學組成，亦可使鈦殘屑1b成為屬於JIS2種之化學組成，亦可作為其以外之化學組成，且將不足之氧或鐵藉由添加副原料1c來調整。 　　[0061] 接著，說明可作為原料使用之副原料1c。 　　[0062] 副原料1c，係為了得到目標之化學組成的鈦塊2，而添加於海綿鈦1a及鈦殘屑1b之1種以上中。例如，添加氧時係將氧化鈦、添加鐵時係將電解鐵粒、欲添加Al時係將Al粒、欲增加Al與V時係將Al-V合金粒、欲增加Fe與Mo時係將Fe-Mo合金，分別作為副原料1c而添加。副原料1c，可僅添加1種、亦可同時添加複數種。 　　[0063] (1-5)副原料之大小 　　副原料1c之大小，較期望為平均粒徑0.1μm以上10mm以下之粉末或粒狀。平均粒徑未達0.1μm之粉末時，搬送或混合如此之微粉之時，容易揚起而飛散至周圍，因此變得無法添加特定的質量。 　　[0064] 另一方面，平均粒徑大於10mm之粒子時，於之後步驟照射電子束可使鈦團塊1熔解的範圍係有所限制，因此無法與海綿鈦1a及鈦殘屑1b均勻熔解，故不佳。 　　[0065] 2.鈦塊 　　如圖2所示，鈦塊2，為將海綿鈦1a壓縮成形為圓柱狀、稜柱狀或多稜柱狀之棒形狀而成為鈦團塊1後，將其表面熔解而得者，其表面具備柱狀組織2a、2b。鈦塊2係如後述，藉由填充於以鈦板材所製作之容器(捆包材料)中，而成為形成鈦扁胚3之材料。或者，鈦塊2，可利用作為熱加工用素材(中間製品)。此時，鈦塊2依其大小或形狀，亦稱為鈦扁胚、鈦胚料或鈦塊料(titanium bloom)。 　　[0066] (2-1)鈦塊之化學組成 　　鈦塊2之化學組成，係藉由作為鈦團塊1之原料所利用的海綿鈦1a及/或鈦殘屑1b之化學組成或其重量比例、所添加之副原料1c之化學組成與其重量比例而決定。因此，係預先藉由化學分析等來掌握海綿鈦1a及鈦殘屑1b、副原料1c之化學組成，藉以可得到目標之鈦塊2之化學組成，並因應其化學組成，求得所必要之各原料之重量。再者，藉由電子束熔解，所揮發去除之元素(例如氯或鎂)，即使含於鈦團塊1中，亦不含於鈦塊2中。 　　[0067] 本發明之鈦塊之化學組成，以質量%計，係O：0.01~0.5%、Fe：0.01~5%、Al：0~8%、Sn：0~5%、Zr：0~12%、Mo：0~15%、Ta：0~2%、V：0~22%、Nb：0~2%、Si：0~1%、Cr：0~10%、Cu：0~0.1%、Co：0~1%、Ni：0~1%、鉑族元素：0~0.5%、REM：0~0.2%、B：0~3%、N：0~0.2%、C：0~2%、H：0~0.013%，剩餘部分為鈦及雜質。 　　[0068] 鉑族元素具體而言，為由Ru、Rh、Pd、Os、Ir及Pt中選擇的一種以上，鉑族元素之含量意指上述元素之合計含量。又，REM為Sc、Y及鑭系元素之合計17個元素之總稱，REM之含量意指上述元素之合計量。 　　[0069] 鈦塊中之剩餘部分之鈦的含量較佳為70%以上。依需要亦可為75%以上、80%以上、85%以上。Al、Sn、Zr、Mo、Ta、V、Nb、Si、Cr、Co、Ni、鉑族元素、REM及B之含有並非必須，各自之含量下限為0%。依需要，Al、Sn、Zr、Mo、Ta、V、Nb、Si、Cr、Co、Ni、鉑族元素、REM及B之各自之含量下限，均亦可為0.01%、0.05%、0.1%、0.2%或0.5%。 　　[0070] O之上限可為0.4%、0.3%、0.2%或0.1%。Fe之上限可為3%、2%、1%或0.5%。Al之含量之上限可為5%、3%、2%或1%。Sn之含量之上限可為3%、2%、1%或0.5%。Zr之含量之上限可為10%、8%、5%或2%。Mo之含量之上限可為12%、9%、4%或2%。Ta之含量之上限可為1%、0.5%、0.2%或0.1%。V之含量之上限可為18%、15%、10%或5%。Nb之含量之上限可為1%、0.5%、0.2%或0.1%。Si之含量之上限可為0.8%、0.5%、0.2%或0.1%。Cr之含量之上限可為8%、5%、2%或1%。Co之含量之上限可為0.8%、0.5%、0.2%或0.1%。Ni之含量之上限可為0.8%、0.5%、0.2%或0.1%。鉑族元素之含量之上限可為0.4%、0.3%、0.2%或0.1%。N之上限可為0.1%、0.05%、0.03%或0.02%。Cu之上限可為0.8%、0.5%、0.2%或0.1%。C之上限可為1%、0.5%、0.2%或0.1%。REM之含量之上限可為0.1%、0.05%、0.03%或0.02%。B之含量之上限可為2%、1%、0.5%或0.3%。 　　各元素之添加目的示於表1。 　　[0071][0072] 鈦塊2較佳係以滿足各種規格所規定之化學組成範圍的方式製造。雖亦有ASTM規格或AMS規格，以下主要以JIS規格為中心，作為代表性的規格進行例示。本發明可使用於此等規格之鈦或鈦合金的製造。 　　[0073] (2-1-1)工業用純鈦 　　工業用純鈦，例示有屬於調整過氧與Fe之JIS1種~JIS4種(JIS H 4600(2012年)鈦及鈦合金-板及條)的工業用純鈦。工業用純鈦，氧與Fe越少則加工性越良好，氧與Fe越多則越高強度。JIS1種係指具有C：0.08%以下、H：0.013%以下、O：0.15%以下、N：0.03%以下、Fe：0.20%以下、剩餘部分Ti及雜質之化學組成的鈦。JIS2種係指具有C：0.08%以下、H：0.013%以下、O：0.20%以下、N：0.03%以下、Fe：0.25%以下、剩餘部分Ti及雜質之化學組成的鈦。JIS3種係指具有C：0.08%以下、H：0.014%以下、O：0.30%以下、N：0.05%以下、Fe：0.30%以下、剩餘部分Ti及雜質之化學組成的鈦。JIS4種係指具有C：0.08%以下、H：0.015%以下、O：0.40%以下、N：0.05%以下、Fe：0.50%以下、剩餘部分Ti及雜質之化學組成的鈦。 　　[0074] (2-1-2)耐蝕鈦合金 　　耐蝕鈦合金，例示有屬於含有Pd、Ru、Ni、Co等之JIS11種~JIS23種(JIS H 4600(2012年)鈦及鈦合金-板及條)的鈦合金。耐蝕鈦合金係耐蝕性及耐間隙腐蝕性優良。 　　[0075] (2-1-3)鈦合金 　　鈦合金，例示有Ti-1.5Al((JIS50種(JIS H 4600(2012年)鈦及鈦合金-板及條))、Ti-6Al-4V(JIS60種(JIS H 4600(2012年)鈦及鈦合金-板及條))、Ti-3Al-2.5V(JIS61種(JIS H 4600(2012年)鈦及鈦合金-板及條))、Ti-4Al-22V(JIS80種(JIS H 4600(2012年)鈦及鈦合金-板及條))等。 　　[0076] Ti-1.5Al係耐蝕性優良、耐氫吸收性及耐熱性優良。 　　[0077] Ti-6Al-4V係高強度且通用性高。 　　[0078] Ti-3Al-2.5V係熔接性、成形性良好，且切削性良好。 　　[0079] Ti-4Al-22V係高強度且冷加工性優良。 　　[0080] 依照本發明，除了上述以外，亦可製造具有JIS中未規定之化學組成的鈦塊2。例如，如以下所列記。 　　[0081] 例示有具有耐熱性之Ti-6Al-2Sn-4Zr-2Mo-0.08Si、Ti-6Al-5Zr-0.5Mo-0.2Si、Ti-8Al-1Mo-1V等； 　　低合金且高強度之Ti-1~1.5Fe-0.3~0.5O-0.01~0.04N等； 　　耐潛變性優良之Ti-6Al-2Sn-4Zr-6Mo等； 　　高強度且冷加工性良好的Ti-15V-3Cr-3Sn-3Al、Ti-20V-4Al-1Sn等； 　　高強度高韌性之Ti-10V-2Fe-3Al等；與 　　耐摩耗性Ti-6Al-4V-10Cr-1.3C等。 　　[0082] (2-2)鈦塊之形狀 　　鈦塊2之形狀係以板狀或柱狀為宜。板狀之鈦塊2的厚度係7~80mm。厚度之上限可為70mm、60mm、50mm或40mm。柱狀之鈦塊2，於垂直於長度方向的截面之形狀，係有圓形的情況與五角形以上之多角形的情況。截面形狀為圓形時，截面之直徑係設為10~80mm。截面之直徑之上限，可為70mm、60mm、50mm或40mm。多角形時，其圓當量直徑係設為10~80mm。圓當量直徑之上限，可為70mm、60mm、50mm或40mm。再者，圓當量直徑，係指相當於截面面積之圓的直徑。 　　[0083] 板狀之鈦塊2的寬度不須特別規定。惟，其下限可為與厚度同等或100mm。其上限可為100mm、500mm、1000mm、2000mm。鈦塊2之長度不須特別規定。惟，其下限可為與板寬、直徑或圓當量直徑同等或100mm。其上限可為500mm、1000mm、3000mm、5000mm、10000mm。 　　[0084] 由於鈦團塊1中有空隙1d，故由鈦團塊1所製作之鈦塊2的體積，較鈦團塊1之體積小。因此，為了得到所期望之尺寸的鈦塊2，必須考慮鈦團塊1之容積比重來決定鈦團塊1之尺寸。 　　[0085] 例如，為了得到厚度50mm之長方體形狀的鈦塊2(容積比重4.5)，只要準備厚度70mm之長方體形狀的鈦團塊1(容積比重3.2)即可。又，為了得到直徑50mm之圓柱形狀的鈦塊2(容積比重4.5)，只要準備直徑60mm之圓柱狀的鈦團塊1(容積比重3.1)即可。 　　[0086] 鈦塊2為板狀時，其厚度未達7mm時，鈦團塊1之厚度亦薄，強度變小。此時，將鈦團塊1移動或反轉等進行操作時會破裂或缺角。另一方面，其厚度大於80mm時，於後述之鈦塊之製造步驟中，必須使鈦團塊1之熔解深度為大。此時，熔解後之冷卻速度變慢，結晶粒會成為大型。又，與以往之熔解步驟同樣地，必須有巨大輸出之電子束。 　　[0087] 鈦塊2為柱形狀時，其直徑(多稜柱形狀的情況時為圓當量直徑)未達10mm時，鈦團塊1之直徑亦小，強度變小。此時，將鈦團塊1移動或旋轉等進行操作時會破裂或折斷。另一方面，其直徑(多稜柱形狀的情況時為圓當量直徑)大於80mm時，於後述之鈦塊之製造步驟中，必須使鈦團塊1之熔解深度為大。此時，其後之冷卻速度變慢，結晶粒會成為大型。又，與以往之熔解步驟同樣地，必須有巨大輸出之電子束。 　　[0088] (2-3)鈦塊之結晶粒的大小 　　鈦塊2為板狀，且厚度7~80mm時，如圖2所示，鈦塊2之金屬組織，係成為自鈦塊2表面朝向厚度方向延伸的柱狀組織2a、2b。於鈦塊2之板寬方向及長度方向的中央部且厚度方向之中央部(圖2中之符號A所示之區域，以下稱為中央區域。再者，中央區域位於板厚方向之中央部)的圓當量平均結晶粒徑為10mm以下，且為鈦塊2之厚度的一半以下。鈦塊2具有直徑10~80mm之圓形的圓柱形狀，或五角形以上之多角形且圓當量直徑(截面積與該多角形之截面積相同之圓的直徑)10~80mm之多稜柱形狀時，如圖3所示，係成為於垂直於鈦塊2之長度方向的截面，自表面朝向面向中心之方向(直徑方向)延伸的柱狀組織30a。於長度方向之中央部且前述截面之中心位置(圖中之符號C所示之區域，以下稱為中心區域)的圓當量平均結晶粒徑為10mm以下，且為鈦塊2之截面直徑的一半以下。藉此，熱加工鈦塊2時即使加工率少亦可容易將結晶粒分隔，可成為製品所必須的細粒。 　　[0089] 再者，對鈦團塊表面照射電子束而熔解之鈦塊，一停止照射即迅速凝固，急速地自表面冷卻。因此，於垂直於鈦塊2之長度方向的截面，係成為自表面朝向該表面之垂直方向呈柱狀延伸的結晶粒。鈦塊(板狀)之厚度，相較於以往之鑄塊(通常200~400mm)，係7~80mm而為較薄，故鈦塊之中央區域亦迅速冷卻。因此，中央區域之平均結晶粒，以圓當量直徑計為10mm以下，且為厚度之一半以下。同樣地，鈦塊(柱狀)之直徑，相較於以往之鑄塊，係7~80mm而為較短，故鈦塊之中心區域亦迅速冷卻。藉此，將鈦塊2熱加工時，即使為小的加工率亦可容易地分隔結晶粒，可成為製品所必須之細粒。 　　[0090] 圖2中，自表面側與背面側所延伸之柱狀組織的長度係大致相同。換言之，自表面側與背面延伸為柱狀之結晶的長度係大致相同。但是，亦可藉由使自表面側與背面側所照射之電子束的輸出變大，來改變來自表面側之柱狀組織的長度與來自背面側之柱狀組織的長度。此時由於板厚中央附近之冷卻速度亦快，因此中央區域之平均結晶粒以圓當量直徑計係10mm以下，且為厚度之一半以下。圖3中，由圓柱表面所延伸的柱狀組織之長度雖為相同，但長度並不一定要為相同。此時，由於中心區域附近之冷卻速度亦快，因此圓柱之中心區域的平均結晶粒以圓當量直徑計為10mm以下，且為直徑之一半以下。又，圖2中，對側面朝向板寬方向照射電子束之結果，短的長度之柱狀組織係由側面向板寬方向延伸。對如此側面之電子束的照射雖為較佳，但只要全部的鈦團塊1能夠熔解，則對側面之電子束照射並非必須。 　　[0091] 平均結晶粒之圓當量直徑的下限並無特殊限定，但為了於鈦塊2使結晶粒徑為小，必須使鈦塊2之厚度為極端地薄。但是，由於限於可製造之鈦塊2厚度，故較期望為0.5mm以上。 　　[0092] 此處作為對象之結晶粒，工業用純鈦或α型鈦合金之情況為α相之結晶粒，α+β二相鈦合金或β型鈦合金之情況為β相之結晶粒。結晶粒，當將垂直於鈦塊2之長度方向的截面研磨後，以氟硝酸蝕刻時，能夠目視或以或放大鏡(擴大鏡)擴大來觀察。觀察鈦塊之中央區域(位於自表面起厚度之1/2的區域)的結晶，求得結晶粒數，將觀察面積除以該結晶粒數，算出每1個結晶之平均面積，求得圓當量直徑，藉以算出平均結晶粒。於觀察100~200個結晶粒之區域描繪圓，以該圓之面積為「觀察面積」，以於該圓內所觀察之結晶粒數目為「結晶粒數」。平均結晶粒徑小，難以目視觀察時，亦可以光學顯微鏡觀察而進行照片攝影，由其組織照片同樣地求得平均結晶粒。 　　[0093] 再者，鈦塊2中，藉由以電子束將鈦團塊之一部分熔解使其依次凝固，最終將鈦團塊全體熔解而凝固。所熔解之範圍，係限定於照射電子束之部分，因此所熔解之鈦塊(鈦團塊)的量僅有少許。因此，於凝固時鈦以外之元素的濃化少，亦即凝固偏析亦小。因此，所添加之鈦以外之元素成分隨場所的變動亦可抑制為小。又，由於係將預先均勻混合之鈦團塊予以部分地依次熔解，故並無鈦原料之熔解不均，即使萬一有電子束照射停止的事故，只要由該位置起再度進行熔解，即不產生任何問題。如此地，亦可抑制如直接扁胚鑄造方法之扁胚長度方向之成分變動。亦即，鈦塊2於長度方向的成分變動少，其化學組成為均勻。 　　[0094] 鈦塊2之成分分析，係由鈦塊2之特定位置採取必要量之分析用試樣，藉由以下列記之任一分析方法進行。 　　JIS H 1612(1993年) 鈦及鈦合金中之氮定量方法 　　JIS H 1614(1995年) 鈦及鈦合金中之鐵定量方法 　　JIS H 1617(1995年) 鈦及鈦合金中之碳定量方法 　　JIS H 1619(2012年) 鈦及鈦合金-氫定量方法 　　JIS H 1620(1995年) 鈦及鈦合金中之氧定量方法 　　JIS H 1621(1992年) 鈦合金中之鈀定量方法 　　JIS H 1622(1998年) 鈦合金-鋁定量方法 　　JIS H 1624(2005年) 鈦合金-釩定量方法 　　JIS H 1625(2005年) 鈦合金-鑭、鈰、鐠及釹定量方法 　　JIS H 1630(1995年) 鈦之發光分光分析方法 　　JIS H 1631(2008年) 鈦合金-螢光X線分析方法 　　JIS H 1632(2014年) 鈦之ICP發光分光分析方法 　　[0095] 圖6為顯示分析用試樣之示意圖。如圖6所示，作為分析用之試樣，係由自鈦塊2之長度方向前端及後端起各50mm之位置(端部區域)的2處，與將其間予以3等分而為各等分之長度的中央位置之3處合計5處進行採取。於鈦塊2之截面，當長方體形狀(扁胚)之鈦塊2的情況時，係由於寬度方向中心之表面與背面的表層2處採取，當圓柱形狀(錠塊)之鈦塊的情況時，係由截面中心對稱之表層2處採取。進一步地，於自長度方向前端及後端起各50mm之位置，亦由厚度中心/直徑方向之中心進行採取。如此地，由合計12處(圖6中之●位置)採取分析用試樣進行分析，化學組成之均勻性，係如下述般評估。 　　[0096] 各元素之含量的最大值CMAX 與最小值CMIN 之差分⊿C，為未達0.2CMIN 或未達0.04%時，評估為均勻。例如，O之測定值的最小值為0.04%、最大值為0.05%時，其差分⊿C(=0.01%)為未達0.04%，因此評估為均勻。又，O之測定值的最小值為0.30%、最大值為0.32%時，其差分⊿C(=0.02%)為未達0.2CMIN (=0.060%)，因此評估為均勻。例如，O之測定值的最小值為0.03%、最大值為0.05%時，其差分⊿C(=0.02%)為未達0.04%，因此評估為均勻。又，O之測定值的最小值為0.30%、最大值為0.35%時，其差分⊿C(=0.05%)為未達0.2CMIN (=0.060%)，因此評估為均勻。 　　[0097] 3.鈦團塊之製造方法 　　鈦團塊1係如圖1所示，為將上述原料1a、1b及副原料1c予以壓縮成形所製作之成形體。 　　[0098] 海綿鈦1a或鈦殘屑1b由於為不定形，故無法直接作為特定形狀(長方體、稜柱或圓柱等)。首先，將必要的海綿鈦1a、鈦殘屑1b及副原料1c置入容器並混合。較鈦容易揮發之元素，由於藉由後段之電子束照射而揮發減少，因此可預先添加考慮了其揮發量之量的元素。 　　[0099] 所混合之原料，係投入與所期望大小之鈦團塊1的截面相同形狀之金屬模，以特定壓力壓縮加工而得到鈦團塊1。壓縮成形時的環境，通常為常溫之大氣(空氣)。 　　[0100] 混合手段無特殊限定，由生產性等之觀點，較期望採取以下說明之手段。 　　[0101] (a)於混合容器中投入特定量之海綿鈦1a、鈦殘屑1b與副原料1c。 　　[0102] (b)於混合容器內攪拌使海綿鈦1a、鈦殘屑1b與副原料1c均勻混合。攪拌方法，係將混合容器於上下方向旋轉、自水平傾斜20~70°於斜方向旋轉、將混合容器於上下方向或水平方向等振動、於混合容器內***攪拌子使攪拌子旋轉等。 　　[0103] (c)攪拌時間雖依混合容器之大小或混合之海綿鈦1a、鈦殘屑1b與副原料1c的量而異，但係1~30分鐘。考慮生產性時，較期望以可於數分鐘均勻混合的方式來決定混合容器之大小或處理量。 　　[0104] (d)所混合之海綿鈦1a、鈦殘屑1b與副原料1c，係由混合容器投入壓縮成形用之壓製金屬模，進行壓縮成形。藉此，可得到副原料1c均勻分散的海綿鈦團塊1。 　　[0105] 鈦團塊1之大小，只要因應鈦塊2之大小或由壓縮加工裝置所限制之金屬模的大小來適當決定即可。 　　[0106] 4.鈦塊2之製造方法 　　本發明之鈦塊2，係如圖2所示，由上述製作之鈦團塊1得到。 　　[0107] (4-1)環境 　　鈦團塊1係容納於腔室內，並將腔室內減壓為1Pa以下。鈦團塊1之內部有多數之內含空氣(氧或氮)的空隙1d，直接熔解時，鈦塊2會氧化、氮化，或殘留氣泡，熱加工後成為破裂或表面瑕疵之原因。因此，係減壓為1Pa以下，以自鈦團塊1之內部空隙1d排除空氣。 　　[0108] 壓力之下限並無特殊限定，但為了使腔室內之壓力極端地小，因提高裝置之氣密性，或增強真空排氣機器等，會使製造成本上昇，故腔室內之壓力下限較期望為1×10-3 Pa。 　　[0109] (4-2)熔解 　　設置於減壓之腔室內的鈦團塊1，係首先對上側面照射電子束，依次被熔解及凝固。詳而言之，係對鈦團塊1之厚度方向的一部分(例如大約一半)2a照射電子束使其依次熔解、凝固。以電子束可熔解的範圍係有限度，因此係移動電子束之照射方向，或移動鈦團塊1，對鈦團塊1之上側面全體照射電子束，使鈦團塊1之厚度方向的一部分2a熔解、凝固。 　　[0110] 之後，使鈦團塊1反轉，以其他面(側面、端面或背面)為上側，將尚未熔解及凝固之厚度方向的剩餘一部分(例如大約一半)2b，同樣地照射電子束，使鈦團塊1之厚度方向的全區域依次熔解及凝固而成為鈦塊。藉此，可得到由表面朝向厚度方向延伸的柱狀組織。圖3所示之圓柱狀鈦團塊1的情況時，將圓周面熔解時，亦可一邊繞圓柱之軸旋轉，一邊照射電子束來成為鈦塊。藉此，可得到於垂直於鈦塊之長度方向之截面，於自表面朝向中心之方向(直徑方向)延伸的柱狀組織。如此地，藉由於熔解時使鈦團塊回轉(板狀團塊之反轉、圓柱狀團塊之旋轉)，可使鈦團塊全部熔解及凝固而成為鈦塊。 　　[0111] 將鈦團塊1之厚度方向的一部分2a熔解時，係調整電子束使得不會熔解鈦團塊1之厚度方向全體或直徑方向全體。若厚度全體或直徑方向全體熔解時(所謂的電子束穿透)，所熔融之鈦會由鈦團塊1之下方流出，無法維持所期望之形狀。 　　[0112] 因此，鈦團塊1之熔解深度係設為之未達鈦團塊1之板厚或未達鈦團塊1之直徑。通常較期望藉由使厚度或直徑之一半左右熔解，且反轉或旋轉使剩餘的一半左右熔解，使鈦團塊1之全體熔解。 　　[0113] 再者，鈦團塊1之大小(寬度或長度)係有限制，因此得到大的鈦塊2時，只要將複數個鈦團塊1並排而以電子束熔解接合即可。又，自空隙1d之空氣去除處理，及以電子束所為之鈦團塊1的熔解處理(亦包含反轉後之熔解)，較佳於減壓下連續地進行。 　　[0114] 5.鈦扁胚3 　　接著，說明使用本發明之鈦塊2的鈦扁胚3與鈦板材4a。 　　[0115] 如圖4或圖5所示，鈦扁胚3，為將上述所得之鈦塊2、20，填充於藉由具有同種之化學組成的鈦板材4a、40a所製作之容器(捆包材料)4、40中，將捆包材料4、40之連接部全部熔接而形成熔接部5、50者。鈦扁胚3，依其大小或形狀亦稱為鈦胚料或鈦塊料，顯示為熱加工用素材(中間製品)。 　　[0116] 本發明之鈦扁胚3，以鈦板材4a所被覆之內部為真空，其係容納本發明之鈦塊2者。 　　[0117] 如圖4所示，本發明之鈦扁胚3，為具備以鈦板材4a所形成之捆包材料4，與填充於捆包材料4內部之鈦塊2的鈦扁胚，捆包材料4之內壓，以絕對壓力計算為10Pa以下，鈦板材4a為具有與鈦塊2同種之化學組成的加工用素材。如前所述，鈦塊2多為以滿足各種規格所規定之化學組成範圍的方式製造。捆包材料4之化學組成，較佳為與對鈦塊2所要求之規格相同的化學組成範圍。亦即，同種意指捆包材料4與鈦塊2為相同規格之化學組成範圍內。 　　[0118] 說明形成捆包材料4之鈦板材4a。 　　[0119] 鈦板材4a，為藉由壓延、擠壓、提拉、鍛造等之熱或冷塑性加工而製造之鈦板或鈦管。鈦板材4a為經塑性加工，因此有表面平滑且組織微細(結晶粒小)的優點。 　　[0120] (5-1)厚度 　　捆包材料4為長方體時，鈦板材4a之厚度雖依所製作之捆包材料4大小而異，但較期望為0.5mm以上30mm以下。捆包材料4越大，越需要強度或剛性，因此使用更厚的鈦板材4a。 　　[0121] 未達0.5mm時有於熱加工前之加熱時捆包材料4變形，或於熱加工初期斷裂的可能性，故不佳。較30mm厚時，鈦板材4a佔鈦扁胚3厚度之比例增大，鈦塊2之填充量變少，因此加工鈦塊2之量少，製造效率差，而不佳。為了減低成本，鈦板材4a之厚度較薄為佳，可為20mm以下、10mm或5mm以下。為了確實防止熱加工初期之斷裂，厚度可為1mm以上、2mm以上或3mm以上。 　　[0122] 進一步地，鈦板材4a之厚度，較期望為鈦扁胚3之厚度之3%以上25%以下。鈦板材4a之厚度，較鈦扁胚3之厚度之3%更薄時，難以保持鈦塊2，熱加工前之加熱時會大幅變形，或者捆包材料4之熔接部5會斷裂。 　　[0123] 另一方面，鈦板材4a之厚度，較鈦扁胚3之厚度之25%更厚時，雖無特別的製造上之問題，但鈦板材4a佔鈦扁胚3之厚度之比例增大，鈦塊2之填充量變少，因此加工鈦塊2之量少，製造效率差，故不佳。 　　[0124] 捆包材料4為管時亦同樣地，雖隨著所製作之捆包材料4大小，鈦板材4a之厚度會相異，但管之厚度較期望為0.5mm以上30mm以下。進一步地，與長方體的情況同樣地，鈦板材4a之厚度，較期望為鈦扁胚3之直徑的3%以上25%以下。又，如圖5所示，亦可藉由於將鈦板材40a彎曲為中空管狀所製作之捆包材料40內部填充鈦塊2，將鈦板材40a之端部熔接形成熔接部50，而成為鈦扁胚30。 　　[0125] (5-2)化學組成 　　捆包材料4必須為與鈦塊2同種之化學組成。此處，同種之化學組成，具體而言，意指屬於JIS之相同規格。例如，鈦塊2之化學組成屬於JIS1種時，捆包材料4亦為屬於JIS1種之化學組成。此處，對鈦塊2所要求之規格，可藉由買賣時或製造時之文件而確認。又，該規格亦有亦可由鈦塊2表面之標示來確認的情況。依需要，可為距鈦塊2之化學組成(實際值)±30%以內、±20%以內、±15%以內、±10%以內、±8%以內、±5%以內或±3%以內。 　　[0126] 如此地，藉由使捆包材料4之化學組成成為與鈦塊2同種之化學組成，可使加工後之鈦扁胚的表層與內部成為同等之化學組成，可直接作為鈦塊操作。 　　[0127] (5-3)捆包材料4之結晶粒的大小 　　鈦板材4a，可藉由實施適度的塑性加工進行熱處理，來調整其結晶粒。用於捆包材料4之鈦板材4a的平均結晶粒，較期望圓當量直徑500μm以下。藉此，將鈦扁胚3熱加工時，可抑制因大型結晶之結晶方位不同所產生的表面瑕疵。 　　[0128] 平均結晶粒之圓當量直徑的下限並無特殊限定，然為了於鈦板材4a使結晶粒徑極端地小，必須使塑性加工時之加工比例為大，由於可作為捆包材料4使用之鈦板材4a之厚度係有限，故較期望為10μm以上、更期望為大於15μm。 　　[0129] 此處作為對象之結晶粒，當工業用純鈦或α型鈦合金的情況時為α相之結晶粒，當β型鈦合金的情況時為β相之結晶粒。α+β二相鈦合金的情況時為α相之集合組織體(α片層、α colony)。α片層為相同結晶方位之α結晶粒的集合體。 　　[0130] 工業用純鈦或α型鈦合金、β型鈦合金之平均結晶粒，係以光學顯微鏡觀察構成捆包材料4之鈦板材4a的包含板厚方向之截面組織進行照片攝影，由其組織照片，藉由根據JIS G 0551(2005)之切斷法，求得鈦板材4a之表層(自表面起至深度0.3mm之區域)的平均結晶粒。 　　[0131] α+β二相鈦合金之平均結晶粒徑(α片層之大小)，係使用EBSD(電子束後方散射繞射；Electron Backscatter Diffraction)，由以下所示方法求得。 　　[0132] 首先，採取以由鈦板材4a所構成之捆包材料4的包含板厚方向之截面為觀察面之試驗片，接著，對於試驗片之觀察面的表層(自表面起至深度0.3mm之區域)，以縱2.4mm橫1.8mm之矩形區域為視野，以測定間隔2.3μm、加速電壓15kV，使用EBSD測定。由所得之測定結果以菊池圖型解析製成PQ(圖型品質)圖與相圖，抽出α相。再者，菊池圖型解析，係排除β相僅以α相為對象進行。接著，以相鄰之EBSD測定點的結晶方位之角度差為15°以下，決定α片層，由該α片層之測定點數求得各α片層之面積，算出圓當量直徑。 　　[0133] 接著說明鈦扁胚3。 　　[0134] (5-4)形狀 　　鈦扁胚3之形狀並無限制，係依所製造的鈦塊之形狀而決定。製造鈦薄板時，鈦扁胚3係為長方體形狀(扁胚)。鈦扁胚3之厚度、寬度及長度，係依製品之厚度、寬度及長度、製造量(重量)等而決定。 　　[0135] 製造鈦圓棒、線材或擠壓型材時，鈦扁胚3為圓柱形或八稜柱等之多稜柱形狀(胚料)。其大小(直徑、長度)係依製品之大小厚度、寬度及長度、製造量(重量)等而決定。 　　[0136] (5-5)內部 　　於鈦扁胚3之內部係填充有鈦塊2。鈦塊2可填充1個或複數個。鈦塊2與捆包材料4之間或鈦塊2彼此之間係有空隙6。該空隙6中若有空氣時，於熱加工前加熱時，所填充之鈦塊2會氧化或氮化，其後加工所得之鈦材會變脆，無法得到必要之材料特性。 　　[0137] 又，填充Ar氣體等之惰性氣體時，可抑制鈦塊2或捆包體6之氧化或氮化，但加熱時Ar氣體會熱膨脹而擠開捆包材料4，鈦扁胚3會變形，無法進行熱加工。 　　[0138] 由以上理由，鈦塊2與捆包材料4之間或鈦塊2彼此之間的空隙，必須極力減壓。具體而言，絕對壓力較期望為10Pa以下、更期望為1Pa以下。 　　[0139] 捆包材料4之內壓大於10Pa時，因所殘留之空氣，鈦塊2或捆包材料4會氧化或氮化。下限並無特殊限定，然為了使內壓極端小，因提高裝置之氣密性，或增強真空排氣機器等，製造成本會上昇，因此內壓之下限較期望為1×10-3 Pa。 　　[0140] 再者，所製作之鈦扁胚3的內壓，可如以下般測定。亦即，可於水中或真空腔室內，對鈦扁胚3開孔，回收內部所殘存氣體(空氣)的全部量，測定其體積，或基於真空度之變化來計算其體積。又、藉由回收侵入內部之水求得其體積，亦可掌握鈦扁胚3內之空隙的體積。藉由本方法，至少可確認鈦扁胚3之內壓為10Pa以下。 　　[0141] (5-6)減壓方法 　　接著，說明將捆包材料4之內部減壓以保持真空的方法。 　　[0142] 捆包材料4，為將鈦塊2填充後，減壓至特定內壓以下而經密閉者。或者亦可將鈦板材4a彼此予以部分接合後，進行減壓、密閉。藉由進行密閉，空氣不會侵入，熱加工前之加熱時內部的鈦塊2或捆包材料4不會被氧化。 　　[0143] 密閉方法並無特殊限定，較佳為將鈦板材4a彼此熔接而密閉。此時，熔接部5係將鈦板材4a之連接部全部熔接而形成，亦即進行全周熔接。將鈦板材4a熔接之方法，係鎢極鈍氣熔接(TIG welding)或金屬惰氣熔接(MIG welding)等之電弧熔接、電子束熔接或雷射熔接等，並無特殊限定。 　　[0144] 熔接之環境，係以鈦塊2及捆包材料4之內面不被氧化或氮化的方式，於減壓下或於惰性氣體環境下進行熔接。將鈦板材4a之連接部最後熔接的情況時，較期望為將捆包材料4置入減壓下之容器(腔室)進行熔接，將捆包材料4之內部保持為減壓狀態。 　　[0145] 其他，亦可預先於捆包材料4之一部分設置配管，於惰性氣體環境下將全周熔接後，通過該配管減壓至特定內壓，將配管以壓接等密封，以使捆包材料4之內部成為減壓狀態。再者，此時，配管只要係於其後步驟之熱加工時不會造成不良狀態的位置，例如後端面上施工即可。 　　[0146] (5-7)加工 　　如以上般所得之較以往更薄或細直徑之鈦塊2或鈦扁胚3，係進行熱加工或冷加工而成為所期望之形狀。加工方法雖依鈦扁胚之形狀而異，但由於均為厚度薄或細直徑，因此可輕易地加工至所期望之大小。 　　[0147] 製造鈦板時，係將長方體形狀(扁胚)之鈦塊2或鈦扁胚3加熱，進行熱壓延以成為鈦板。依需要，亦可與以往步驟同樣地，以酸洗等去除氧化層後，進行冷壓延，而加工為更薄。 　　[0148] 製造鈦圓棒或線材時，係將圓柱或多稜柱形狀之鈦塊2或鈦扁胚3加熱，進行熱鍛造、熱壓延或熱擠壓，成為鈦圓棒或線材。又，依需要，亦可與以往步驟同樣地，以酸洗等去除氧化層後，進行冷壓延等，而加工為更細。製造鈦擠壓型材時，係將圓柱或多稜柱形狀之鈦塊2或鈦扁胚3加熱，進行熱擠壓，成為各種截面形狀之鈦型材。 　　[0149] 使用鈦塊2時，可能有於熱加工後之板或圓棒、型材的表面產生疤狀缺陷的情況。此時，係將表面以切削、酸洗等來去除表面缺陷。 　　[0150] 使用鈦扁胚3時，熱加工後之板或圓棒、型材的表面為良好，不須處理表面。 [實施例1] 　　[0151] 接著，說明本發明之實施例。 　　[0152] 作為原料之鈦源，係使用以克羅爾法製造之海綿鈦(粒度=0.25mm以上19mm以下)，氧含量0.03%、鐵含量0.02%、氮含量0.002%、碳含量0.001%、氫含量0.001%。又，作為鈦殘屑，一部分(參照表1之No.11、12)係使用將JIS1種(氧含量0.04%、鐵含量0.03%、氮含量0.001%、碳含量0.003%、氫含量0.007%)之薄板切斷為20~30mm見方者。 　　[0153] 作為副原料，係依鈦塊之目標化學組成適當使用氧化鈦粉、電解鐵、Pd粉粒、Al粒、Al-V合金粒、Sn粒、Zr粒、Mo粉、Ta粉、Nb粉、Si粉、Cr粒、Co粒、Ni粒、Ru粉、Mm(密鈰合金)粉、FeN粉、C粉、TiB2 粉。再者，Al-V合金粒為Al含量30%、V含量70%之合金。Mm係使用主要由La(鑭)、Ce(鈰)、Nd(釹)所構成的混合物。 　　[0154] 將海綿鈦、鈦殘屑或副原料投入不鏽鋼製之混合容器中，將該混合容器於上下方向旋轉以進行原料混合。藉由將混合後之原料投入特定量於角狀金屬模中，並壓縮成形而製作長方體形狀之鈦團塊。此時，由鈦團塊之大小與重量所求得的空隙率為28~45%。 　　[0155] 將所得之鈦團塊置入真空腔室，將鈦團塊之上側面以電子束熔解鈦團塊之厚度的一半更多2~3mm。該熔解之量(厚度)，係預先求得電子束之輸出與可熔解之厚度的關係，由該結果，由必要之厚度求得電子束之輸出。使鈦團塊之上側面凝固及冷卻後，將鈦團塊反轉，將背面同樣地熔解。 　　[0156] 如此地，使鈦團塊全體熔解/凝固，製作寬度300mm、長度1200mm之各種厚度的長方體之鈦塊。 　　[0157] 亦製作僅將鈦塊之表層附近熔解，內部並未使原料熔解之鈦塊，作為比較例(參照表1之No.25、26)。所有的例子中，所熔解的表層之厚度，於各面均為4~8mm。 　　[0158] 將所得之鈦塊一部分切斷來進行成分分析，評估其均質性。剩餘的鈦塊係進行熱壓延，成為厚度3.5~8.0mm之壓延板。 　　[0159] 作為習知例，係以具有冷爐床之EB熔解爐得到鈦鑄塊。亦即，將海綿鈦與氧化鈦、電解鐵、Al粒作為原料投入冷爐床中，對原料照射電子束，將熔融之鈦注入厚度250mm之模具得到鈦鑄塊。熔解初期係以0.35ton/h之熔解速度開始，慢慢增加熔解速度，於恆定部係以0.75ton/h熔解。之後，慢慢降低熔解速度，熔解末期係降至0.2ton/h後，結束熔解，得到長度1200mm之鈦鑄塊。 　　[0160] 目視或使用金屬顯微鏡測定鈦塊之中心部的結晶粒徑。又，鈦塊之成分分析，係自鈦塊之特定位置採取必要量之分析用試樣，藉由以下列記之任一分析方法進行。 　　JIS H 1612(1993年) 鈦及鈦合金中之氮定量方法 　　JIS H 1614(1995年) 鈦及鈦合金中之鐵定量方法 　　JIS H 1617(1995年) 鈦及鈦合金中之碳定量方法 　　JIS H 1619(2012年) 鈦及鈦合金-氫定量方法 　　JIS H 1620(1995年) 鈦及鈦合金中之氧定量方法 　　JIS H 1621(1992年) 鈦合金中之鈀定量方法 　　JIS H 1622(1998年) 鈦合金-鋁定量方法 　　JIS H 1624(2005年) 鈦合金-釩定量方法 　　JIS H 1625(2005年) 鈦合金-鑭、鈰、鐠及釹定量方法 　　JIS H 1630(1995年) 鈦之發光分光分析方法 　　JIS H 1631(2008年) 鈦合金-螢光X線分析方法 　　JIS H 1632(2014年) 鈦之ICP發光分光分析方法 　　[0161] 由自鈦塊2之長度方向之前端及後端起各50mm的位置(端部區域)之2處，與將其間3等分且各等分長度之中央位置的3處合計5處進行採取，作為分析用試樣。於鈦塊2之截面，當長方體形狀(扁胚)之鈦塊2的情況時，係在於寬度方向中心之表面與背面的表層2處採取，當圓柱形狀(錠塊)之鈦塊的情況時，係由截面中心對稱之表層2處採取。進一步地，於自長度方向前端及後端起各50mm之位置，亦由厚度中心/直徑方向之中心採取。如此地，由合計12處(圖6中●的位置)採取分析用試樣進行分析，化學組成之均勻性係如下述般評估。 　　[0162] 各元素之含量的最大值CMAX 與最小值CMIN 之差分⊿C，當未達0.2CMIN 或未達0.04%時，評估為均勻性良好。例如，O之測定值的最小值為0.04%、最大值為0.05%時，其差分⊿C(=0.01%)未達0.04%，因此評估為均勻性良好。又，O之測定值的最小值為0.30%、最大值為0.32%時，其差分⊿C(=0.02%)為未達0.2CMIN (=0.060%)，因此評估為均勻性良好。 　　[0163] 又，於自長度方向前端及後端起各50mm之位置，係使用目視或金屬顯微鏡測定厚度中心部之結晶粒徑，求得其平均值。剩餘的鈦塊係進行熱壓延，成為厚度3.5mm至8mm之板。 　　[0164] 　　實施例1中，鈦塊之製作條件歸納示於表2、所製作之鈦塊歸納示於表3、將鈦塊壓延所製作之鈦材(壓延板)歸納示於表4。 　　[0165][0166][0167][0168] 如表2~表4所示，No.1~8為改變鈦團塊之厚度與空隙率，以各種厚度製作鈦塊者。 　　[0169] No.1，當鈦團塊之厚度薄至8mm時雖可得到厚度5.7mm之薄的鈦塊，但鈦團塊之一部分的角缺損，故無法壓延。 　　[0170] 其以外之厚度的No.2~8，化學組成為均質，鈦塊之厚度中心的結晶粒徑小至0.8~7.8mm，壓延亦可無問題地進行，於壓延板之表面的一部分雖產生表面瑕疵，但大致良好。於一部分產生之表面瑕疵可部分地處理而去除。 　　[0171] No.8~10分別為製作JIS1種、JIS3種、JIS4種之壓延板的情況，No.11、12為一部分或全部使用JIS1種之鈦殘屑，來製作JIS2種、JIS3種之壓延板的情況。 　　[0172] 此等所有的情況，均為成分變動少的均質，可得到中心之結晶粒徑小的鈦塊，之後之壓延亦可無問題地進行。於壓延板之表面的一部分雖產生表面瑕疵，但大致良好。 　　[0173] No.13~24，為添加Fe及Fe以外之各種金屬元素作為副原料的情況。此等所有的情況，均為成分變動少的均質，可得到中心之結晶粒徑小的鈦塊，之後之壓延亦可無問題地進行。於壓延板之表面的一部分雖產生表面瑕疵，但大致良好。 　　[0174] 比較例之No.25、26中，係製作將鈦團塊之表層附近熔解，內部則不使原料(海綿鈦、副原料)熔解而直接留下之鈦塊。此等鈦塊之厚度中心部因並未熔解，故自長度方向之前端及後端起各50mm之位置(端部區域)的2處之中心部係維持為鈦團塊。因此，無法進行中心部之分析及結晶粒徑之測定故省略。亦即，分析為由自熔解之鈦塊表層部所採取的10個部位來評估化學組成之均勻性。 　　[0175] 此等之鈦塊，氧或Fe等之鈦以外的添加元素係隨著鈦塊之位置而有大幅變動，成為不均質的鑄塊。進一步地，將該鑄塊壓延後，伴隨該成分之不均質，於高溫之變形阻力會大幅不同，因此產生多數之大的表面破裂。因此，無法作為製品使用。 　　[0176] 再者，No.1~No.26之全部的比較例及本發明例中鈦之含量為70%以上。又，於海綿鈦或鈦殘屑中作為雜質而含有的碳、氮或氫，係含有於全部的比較例及本發明例中。 　　[0177] 習知例之No.27為將工業用純鈦(JIS2種)以習知法熔解之結果，扁胚係250mm而為較大，因此因凝固偏析，Fe成分之偏差大，厚度中心之結晶粒亦為13mm而較大。又，壓延後之薄板產生多量之疤狀的表面瑕疵。No.28為將Ti-5Al-1Fe合金熔解之結果，扁胚係250mm而為較大，因此因凝固偏析，Fe成分之偏差大，厚度中心之結晶粒亦為12mm而較大。又，因Al揮發量之偏差，Al成分之變動亦大。進一步地，壓延後之薄板產生多量之疤狀的表面瑕疵。 [實施例2] 　　[0178] 使用與實施例1之No.4同樣地製作的厚度35mm、寬度300mm、長度400mm之鈦塊，製作鈦扁胚。 　　[0179] 鈦捆包材料，係使用與厚度1~20mm之鈦塊相同的JIS2種材。於壓延鈦扁胚時作為不與壓延輥接觸之容器的側面之1枚鈦捆包材料上，將具有閥之配管予以鎢極鈍氣熔接而固定。配管之閥係關閉。將包含熔接有該配管之鈦捆包材料的5枚鈦捆包材料臨時組裝而作為容器後，於其中容納鈦塊，以剩餘的鈦捆包材料加蓋。將臨時組裝的捆包體置入真空腔室內，減壓(真空)至特定壓力後，將捆包材料之連接部以全周電子束熔接而製作鈦扁胚(參照表5之No.2、3、5)。於位於所製作之鈦扁胚側面的配管設置真空計，打開閥以測定內壓。測定後將該配管於鈦扁胚與閥之間進行密閉，將閥切斷去除。 　　[0180] 又，以鎢極鈍氣熔接來組裝鈦扁胚後，由設置於鈦捆包材料之排氣用配管，減壓(真空)至鈦扁胚內部成為特定壓力後，將排氣用配管密閉，藉以調整鈦扁胚之內壓。 　　[0181] 將此等之厚度37~75mm之鈦扁胚壓延，製作厚度4.0~5.5mm之壓延板。 　　[0182] 實施例2之結果與試驗條件一併歸納示於表5。 　　[0183][0184] 如表5所示，使鈦扁胚之內壓為10Pa以下之No.1~3，可無問題地壓延，所得之壓延板的表面亦為良好。 　　[0185] 使鈦扁胚之內壓為12Pa之No.4，雖可無問題地壓延，但所得之壓延板一部分係裂為二枚而產生剝離。觀察產生剝離之部分時，可知鈦塊與鈦捆包材料之表面係氧化，兩材料未壓接。 　　[0186] 同樣地，使用與實施例1之No.14同樣地製作之鈦塊，來製作鈦扁胚。 　　[0187] 鈦捆包材料，係使用與厚度10mm之鈦塊相同的Ti-5Al-1Fe材(數字為質量%)。將5枚鈦捆包材料予以臨時組裝而成為容器後，於其中容納鈦塊，以剩餘的鈦捆包材料加蓋。 　　[0188] 將臨時組裝的捆包體置入真空腔室內，減壓(真空)至特定壓力後，將捆包材料之連接部以全周電子束熔接而製作鈦扁胚(No.5)。 　　[0189] 將該鈦扁胚壓延，製作厚度5.0mm之壓延板。可無問題地進行壓延，所得之壓延板的表面亦為良好。 [實施例3] 　　[0190] 作為原料之鈦源，係使用以克羅爾法製造之海綿鈦(粒度=0.25mm以上19mm以下)，氧含量0.04%、鐵含量0.03%、氮含量0.003%、碳含量0.003%、氫含量0.001%。又，作為鈦殘屑，一部分(參照表3之No.10、11)係使用將 JIS1種(氧含量0.04%、鐵含量0.03%、氮含量0.003%、碳含量0.004%、氫含量0.003%)之薄板切斷為20~30mm見方者。 　　[0191] 作為副原料，係依鈦塊之目標成分適當使用氧化鈦粉、電解鐵、Pd粉粒、Al粒、Al-V合金粒、Sn粒、Zr粒、Mo粉、Ta粉、Nb粉、Si粉、Cr粒、Co粒、Ni粒、Ru粉、Mm(密鈰合金)粉、FeN粉、C粉、TiB2 粉。再者，Al-V合金粒為Al含量30%、V含量70%之合金。 　　[0192] 將海綿鈦、鈦殘屑或副原料投入不鏽鋼製之混合容器中，將該混合容器於上下方向旋轉以進行原料混合。將混合後之原料投入特定量於圓柱狀之金屬模中，並壓縮成形，藉以製作3個圓柱形狀之鈦團塊(長度300mm)。此時，由鈦團塊之大小與重量所求得的空隙率為28~40%。 　　[0193] 將所得之鈦團塊3個於長度方向並排並置入真空腔室中，將鈦團塊之周面以電子束熔解鈦團塊直徑之一半更多2~3mm。該熔解之量(直徑)，係預先求得電子束之輸出與可熔解之厚度的關係，由該結果，由必要之厚度求得電子束之輸出。一邊使鈦團塊旋轉，一邊使周面全體熔解及凝固。 　　[0194] 如此地，使鈦團塊全體熔解及凝固，製作長度900mm且直徑9~78mm之圓柱狀的鈦塊。化學組成之均勻性及結晶粒徑，係與(實施例1)同樣地評估。 　　[0195] 作為習知例，係以具有冷爐床之EB熔解爐得到鈦鑄塊。亦即，將海綿鈦與氧化鈦、電解鐵、Al粒作為原料，投入冷爐床中，對原料照射電子束，將熔融之鈦注入直徑600mm之模具。熔解初期係以0.5ton/h之熔解速度開始，慢慢增加熔解速度，於恆定部係以0.85ton/h進行熔解。之後，慢慢降低熔解速度，於熔解末期降至0.3ton/h後，結束熔解，得到長度900mm之鈦鑄塊。對該鈦鑄塊係採取分析用試樣及組織觀察用試樣後，鍛造至φ100mm，進一步壓延而成為φ30mm之圓棒。 　　[0196] 實施例3中，鈦塊之製作條件歸納示於表6、所製作之鈦塊歸納示於表7、將鈦塊壓延所製作之鈦材(圓棒)歸納示於表8。 　　[0197][0198][0199][0200] 如表6~表8所示，作為比較例，於No.22亦製作僅將鈦塊之表層附近熔解，內部不使原料熔解之鈦塊。 　　[0201] 所得之鈦塊係與實施例1同樣地採取分析用試樣進行化學組成分析，藉由與實施例1相同之手法評估其均質性。又，於長度方向中央部，使用目視或金屬顯微鏡測定垂直於長度方向之截面中心部的結晶粒徑。剩餘的鈦塊係進行熱壓延，成為直徑8mm至18mm之圓棒。 　　[0202] 表6~表8中之No.1~6，係改變鈦團塊之直徑與空隙率，製作各種直徑之鈦塊的情況。鈦團塊之直徑細至11mm時雖可得到直徑9mm之細的鈦塊，但鈦團塊之一部分折損，因此無法壓延(No.1)。其以外之直徑的鈦塊可無問題地壓延，可得到良質之圓棒(No.2~6)。 　　[0203] No.7~9，為製作JIS1種、JIS3種、JIS4種之鈦塊的情況，No.10、11係一部分或全部使用JIS1種之鈦殘屑，來製作JIS2種、JIS3種之壓延板的情況。此等中所有的情況，均為化學組成之變動少的均質，可得到中心之結晶粒徑小的鈦塊，之後之壓延亦無問題，可得到良質之圓棒。 　　[0204] No.12~21為添加Fe及Fe以外之各種金屬元素作為副原料的情況。此等中所有的情況，均為成分之變動少的均質，可得到中心之結晶粒徑小的鈦塊，之後之壓延亦可無問題地進行，可製造良質之圓棒。 　　[0205] 比較例之No.22中，係製作將鈦團塊之表層附近熔解，內部則不使原料(海綿鈦、副原料)熔解而直接留下的直徑44mm之鈦塊。該鈦塊之厚度中心部因並未熔解，故自長度方向之前端及後端起各50mm之位置(端部區域)之2處的中心部係維持為鈦團塊。因此，無法進行中心部之分析及結晶粒徑之測定，故予以省略。亦即，分析係由自熔解之鈦塊表層部所採取的10個部位來評估化學組成之均勻性。 　　[0206] 分析該鈦塊之化學組成後，作為副原料所添加之氧或Fe會隨著鈦塊之位置而大幅變動，成為不均質的鑄塊。進一步地，將鑄塊壓延後，伴隨該化學組成之不均質，於高溫之變形阻力會大幅不同，因此產生多數之大的表面破割。因此，無法作為製品使用。 　　[0207] 再者，No.1~No.22之全部的比較例及本發明例中鈦之含量為70%以上。又，於海綿鈦或鈦殘屑中作為雜質而含有的碳、氮或氫，係含有於全部的比較例及本發明例中。 　　[0208] 習知例之No.23為將工業用純鈦(JIS2種)以習知法熔解的結果，錠塊徑係600mm而為較大，因此因凝固偏析，Fe成分之偏差大，厚度中心之結晶粒亦為14mm而較大。又，鍛造時產生多量之表面破裂，因此必須將該部分切削去除，製造良率大幅降低。No.24為將Ti-6Al-4V合金以習知法熔解的結果，錠塊徑係600mm而較大，因此因凝固偏析，Fe成分之偏差大，厚度中心之結晶粒亦為13mm而較大。又，因Al揮發量之偏差，Al成分之變動亦大。又，鍛造時產生多量之表面破裂，因此必須將該部分切削去除，製造良率大幅降低。 [產業上之可利用性] 　　[0209] 依照本發明，可省略以往之熔解步驟與鍛造步驟，來製造各種化學組成之厚度薄或細直徑之鈦塊，亦可削減於之後步驟之熱加工中的加工量來製造鈦塊。因此，可削減製造所需之能源。進一步地，藉由成為鈦扁胚，可省略將鈦塊表面所產生之缺陷切削去除，可大幅提高製造良率、大幅減低製造成本。[0047] The raw materials, titanium agglomerates, titanium blocks, and titanium flat embryos used in the present invention will be sequentially described with reference to the accompanying drawings. In addition, in the following description, the "%" of the chemical composition means "% by mass" unless otherwise specified. 1 is an explanatory view schematically showing a titanium agglomerate 1, FIG. 2 is an explanatory view schematically showing a titanium block 2, and FIGS. 4 and 5 are explanatory views schematically showing titanium flat embryos 3, 30. [0049] As shown in FIG. 1, the titanium agglomerate 1 is one or more of sponge titanium 1a and titanium residue 1b, and contains elements necessary for achieving the function as a final product (for example, oxygen, Fe, Al, V). The auxiliary raw material 1c is mixed, for example, by compression molding into a rectangular parallelepiped shape. [0050] 1. Raw material of titanium agglomerate 1 First, the raw material of titanium agglomerate 1 will be described. The raw material of the titanium agglomerate 1 contains at least one of titanium sponge 1a and titanium residue 1b, and contains an auxiliary material 1c which selectively contains various elements. (1-1) Size of Sponge Titanium When the sponge titanium 1a is used as a raw material of the titanium agglomerate 1, a person who has been subjected to a melting step such as a conventional Kroll process can be used. The sponge titanium 1a obtained by the smelting step is usually a bulk of up to several tons, and therefore it is more desirable to use a crushed grain as in the conventional step. [0052] The size of the titanium sponge 1a is preferably 1 mm or more and 25 mm or less in terms of the average particle diameter (however, when used in a plate-shaped titanium block, it is below the thickness of the titanium block; when used in a polygonal prism or a cylindrical titanium block, It is below the diameter of the titanium block). When the average particle diameter is less than 1 mm, it takes time to break, and a large amount of fine dust is generated and scattered, so that the production efficiency is lowered. On the other hand, when the average particle diameter is more than 25 mm, the range in which the titanium agglomerate 1 is melted by irradiating the electron beam in the subsequent step is limited, and there is a possibility that the auxiliary material 1c cannot be uniformly melted. (1-2) Chemical Composition of Sponge Titanium Sponge Titanium 1a is a raw material of titanium block 2, and contains oxygen, iron, nitrogen, carbon, hydrogen, chlorine, magnesium, and the like in addition to titanium. Specifically, it is 0.40% or less of oxygen, 0.50% or less of iron, 0.05% or less of nitrogen, 0.08% or less of carbon, 0.013% or less of hydrogen, 0.10% or less of chlorine, and 0.10% or less of magnesium. [0054] These amounts are desirably equal to or less than the amount required for the titanium block 2. The amount of the element other than titanium contained in the sponge titanium 1a can be directly used as the titanium sponge 1a as long as it is equivalent to the amount required for the titanium block 2. When the amount of the element other than titanium contained in the titanium sponge 1a is less than the amount of the element other than the titanium required for the titanium block 2, it may be added by adding the auxiliary material 1c necessary for the chemical composition. [0055] The amount of the element other than titanium contained in the titanium sponge 1a is more than the amount of the element other than the titanium required for the titanium block 2, and the amount of the sponge titanium 1a is less than the amount required for the titanium block 2. Further, other sponge titanium having a small amount of elements other than titanium is appropriately mixed to dilute an element other than titanium. Thereby, the target titanium block 2 can be obtained. However, when the amount of the element other than titanium of the titanium sponge 1a is too large, it cannot be used because it cannot be diluted. [0056] Next, the titanium residue 1b which can be used as a raw material will be described. [0057] The titanium residue 1b refers to a titanium cut powder which is produced in the titanium material manufacturing step and which is not a product, or which is produced by cutting or grinding in order to make the titanium material into a product shape; After the titanium, etc. (1-3) The size of the titanium residue The size of the titanium residue 1b is preferably 1 mm or more and 25 mm or less in terms of the average particle diameter, similarly to the titanium sponge 1a (however, when used for a plate-shaped titanium block) Below the thickness of the block, it is used for polygonal columnar or cylindrical titanium blocks below the diameter of the titanium block). When the average particle diameter is less than 1 mm, it takes time to break, and a large amount of fine dust is generated and scattered, so that the production efficiency is lowered. On the other hand, when the average particle diameter is more than 25 mm, the range in which the titanium agglomerate 1 is melted by irradiating the electron beam in the subsequent step is limited, and there is a possibility that the auxiliary auxiliary material 1c cannot be uniformly melted. [0059] The titanium residue 1b may be filled in the metal mold in its original state, but the titanium cut powder having a small specific gravity may be preliminarily compressed in order to be filled more efficiently or in a larger amount. The volume specific gravity is increased or mixed with the sponge titanium 1a and then filled. (1-4) The chemical composition of the titanium residue, the titanium residue 1b, when mixed with the titanium sponge 1a, preferably corresponds to the JIS 1 species, the JIS 2 species, the JIS 3 species, or the JIS 4 species of the same species as the sponge titanium 1a. (JIS H 4600 (2012) Titanium and titanium alloys - plates and strips) chemical composition. The titanium residue 1b may also be of the same chemical composition as the target of the titanium block 2. Here, the chemical composition of the same kind, specifically, refers to the same specification as JIS. For example, when the chemical composition of the titanium sponge 1a belongs to the JIS type, the mixed titanium residue 1b may be a chemical composition belonging to the JIS type. Or, in order to obtain the titanium block 2 which belongs to the chemical composition of the JIS type 2, the titanium sponge 1a may be a chemical composition belonging to JIS, and the titanium residue 1b may be a chemical composition belonging to two types of JIS, or may be a chemical composition other than the chemical composition of the JIS. And the insufficient oxygen or iron is adjusted by adding the auxiliary material 1c. Next, an auxiliary material 1c which can be used as a raw material will be described. The auxiliary material 1c is added to one or more of the titanium sponge 1a and the titanium residue 1b in order to obtain the titanium block 2 having the chemical composition of the target. For example, when oxygen is added, titanium oxide is added, iron is added, iron is added, Al is added, Al is added, and when Al and V are added, Al-V alloy is added, and when Fe and Mo are to be added, Fe-Mo alloys were added as the auxiliary materials 1c, respectively. The auxiliary material 1c may be added alone or in combination of plural kinds. (1-5) Size of the auxiliary material The size of the auxiliary material 1c is preferably a powder or a granular shape having an average particle diameter of 0.1 μm or more and 10 mm or less. When the powder having an average particle diameter of less than 0.1 μm is transported or mixed with such a fine powder, it is likely to be lifted up and scattered to the surroundings, so that it is impossible to add a specific mass. On the other hand, in the case of particles having an average particle diameter of more than 10 mm, the range in which the titanium agglomer 1 is melted by irradiating the electron beam in the subsequent step is limited, and thus it is impossible to uniformly melt the titanium sponge 1a and the titanium residue 1b. It is not good. 2. As shown in FIG. 2, the titanium block 2 is obtained by compression-molding the titanium sponge 1a into a rod shape of a columnar shape, a prismatic shape or a polygonal prism shape to form a titanium agglomerate 1, and then melting the surface thereof. In addition, the surface has columnar structures 2a and 2b. The titanium block 2 is a material for forming the titanium flat blank 3 by being filled in a container (packaging material) made of a titanium plate as will be described later. Alternatively, the titanium block 2 can be used as a material for thermal processing (intermediate product). At this time, the titanium block 2 is also referred to as a titanium flat embryo, a titanium billet or a titanium bloom depending on its size or shape. (2-1) Chemical composition of titanium block The chemical composition of the titanium block 2 is a chemical composition of the titanium sponge 1a and/or the titanium residue 1b used as a raw material of the titanium agglomerate 1 or a weight ratio thereof The chemical composition of the added auxiliary material 1c is determined by the ratio of its weight. Therefore, the chemical composition of the titanium sponge 1a, the titanium residue 1b, and the auxiliary material 1c is grasped by chemical analysis or the like in advance, whereby the chemical composition of the target titanium block 2 can be obtained, and the chemical composition is required to obtain the necessary composition. The weight of each raw material. Further, the element (for example, chlorine or magnesium) which is volatilized by electron beam melting is not contained in the titanium block 2 even if it is contained in the titanium agglomerate 1. [0067] The chemical composition of the titanium block of the present invention is, in mass%, O: 0.01 to 0.5%, Fe: 0.01 to 5%, Al: 0 to 8%, Sn: 0 to 5%, Zr: 0~ 12%, Mo: 0~15%, Ta: 0~2%, V: 0~22%, Nb: 0~2%, Si: 0~1%, Cr: 0~10%, Cu: 0~0.1 %, Co: 0~1%, Ni: 0~1%, platinum group elements: 0~0.5%, REM: 0~0.2%, B: 0~3%, N: 0~0.2%, C: 0~ 2%, H: 0~0.013%, the remainder is titanium and impurities. Specifically, the platinum group element is one or more selected from the group consisting of Ru, Rh, Pd, Os, Ir, and Pt, and the content of the platinum group element means the total content of the above elements. Further, REM is a general term for a total of 17 elements of Sc, Y, and a lanthanoid element, and the content of REM means the total amount of the above elements. [0069] The content of titanium in the remaining portion of the titanium block is preferably 70% or more. It may be 75% or more, 80% or more, or 85% or more as needed. The contents of Al, Sn, Zr, Mo, Ta, V, Nb, Si, Cr, Co, Ni, a platinum group element, REM and B are not essential, and the lower limit of each is 0%. The lower limit of the content of each of Al, Sn, Zr, Mo, Ta, V, Nb, Si, Cr, Co, Ni, platinum group elements, REM and B may also be 0.01%, 0.05%, 0.1%. , 0.2% or 0.5%. [0070] The upper limit of O may be 0.4%, 0.3%, 0.2%, or 0.1%. The upper limit of Fe may be 3%, 2%, 1% or 0.5%. The upper limit of the content of Al may be 5%, 3%, 2% or 1%. The upper limit of the content of Sn may be 3%, 2%, 1% or 0.5%. The upper limit of the Zr content may be 10%, 8%, 5% or 2%. The upper limit of the content of Mo may be 12%, 9%, 4% or 2%. The upper limit of the content of Ta may be 1%, 0.5%, 0.2% or 0.1%. The upper limit of the content of V may be 18%, 15%, 10% or 5%. The upper limit of the content of Nb may be 1%, 0.5%, 0.2% or 0.1%. The upper limit of the Si content may be 0.8%, 0.5%, 0.2% or 0.1%. The upper limit of the content of Cr may be 8%, 5%, 2% or 1%. The upper limit of the content of Co may be 0.8%, 0.5%, 0.2% or 0.1%. The upper limit of the content of Ni may be 0.8%, 0.5%, 0.2% or 0.1%. The upper limit of the content of the platinum group element may be 0.4%, 0.3%, 0.2% or 0.1%. The upper limit of N may be 0.1%, 0.05%, 0.03% or 0.02%. The upper limit of Cu may be 0.8%, 0.5%, 0.2% or 0.1%. The upper limit of C can be 1%, 0.5%, 0.2% or 0.1%. The upper limit of the content of REM may be 0.1%, 0.05%, 0.03% or 0.02%. The upper limit of the content of B may be 2%, 1%, 0.5% or 0.3%. The purpose of addition of each element is shown in Table 1. [0071] [0072] The titanium block 2 is preferably manufactured in such a manner as to satisfy the chemical composition range specified by various specifications. The ASTM standard or the AMS standard is also used. The following is mainly based on the JIS standard and is exemplified as a representative standard. The present invention can be used in the manufacture of titanium or titanium alloys of these specifications. (2-1-1) Pure titanium for industrial use of pure titanium, exemplified by JIS type 1 to JIS which are adjusted for peroxygen and Fe (JIS H 4600 (2012) Titanium and Titanium Alloy - Plate and Strip) Industrial pure titanium. For industrial pure titanium, the less oxygen and Fe, the better the processability, and the more oxygen and Fe, the higher the strength. The JIS 1 type refers to titanium having a chemical composition of C: 0.08% or less, H: 0.013% or less, O: 0.15% or less, N: 0.03% or less, Fe: 0.20% or less, and the remaining portion of Ti and impurities. The JIS 2 species refers to titanium having a chemical composition of C: 0.08% or less, H: 0.013% or less, O: 0.20% or less, N: 0.03% or less, Fe: 0.25% or less, and the remaining portion of Ti and impurities. The JIS 3 species refers to titanium having a chemical composition of C: 0.08% or less, H: 0.014% or less, O: 0.30% or less, N: 0.05% or less, Fe: 0.30% or less, and the remaining portion of Ti and impurities. The JIS 4 type refers to titanium having a chemical composition of C: 0.08% or less, H: 0.015% or less, O: 0.40% or less, N: 0.05% or less, Fe: 0.50% or less, and the remaining portion of Ti and impurities. (2-1-2) Corrosion-resistant titanium alloy corrosion-resistant titanium alloy, exemplified by JIS 11 kinds to JIS type 23 containing Pd, Ru, Ni, Co, etc. (JIS H 4600 (2012) Titanium and Titanium Alloy-Board and Article) of titanium alloy. The corrosion-resistant titanium alloy is excellent in corrosion resistance and crevice corrosion resistance. (2-1-3) Titanium alloy titanium alloy, exemplified by Ti-1.5Al ((JIS 50 kinds (JIS H 4600 (2012) titanium and titanium alloy-plate and strip)), Ti-6Al-4V ( JIS 60 species (JIS H 4600 (2012) Titanium and Titanium Alloys - Sheets and Strips)), Ti-3Al-2.5V (JIS 61 species (JIS H 4600 (2012) Titanium and Titanium Alloys - Sheets and Strips)), Ti -4Al-22V (JIS 80 (JIS H 4600 (2012) Titanium and Titanium Alloy - Plate and Strip)), etc. [0076] Ti-1.5Al is excellent in corrosion resistance, hydrogen absorption resistance, and heat resistance. Ti-6Al-4V is high in strength and high in versatility. [0078] Ti-3Al-2.5V is excellent in weldability and formability, and has good machinability. [0079] Ti-4Al-22V is high strength and cold workability According to the present invention, in addition to the above, a titanium block 2 having a chemical composition not defined in JIS can be produced, for example, as listed below. [0081] An example of heat-resistant Ti-6Al-2Sn is exemplified. -4Zr-2Mo-0.08Si, Ti-6Al-5Zr-0.5Mo-0.2Si, Ti-8Al-1Mo-1V, etc.; low alloy and high strength Ti-1~1.5Fe-0.3~0.5O-0.01~0.04 N, etc.; Ti-6Al-2Sn-4Zr-6Mo with excellent resistance to latent denaturation; Ti-15V-3Cr-3Sn-3Al, Ti-20V with high strength and good cold workability -4Al-1Sn, etc.; high strength and high toughness Ti-10V-2Fe-3Al, etc.; and wear resistance Ti-6Al-4V-10Cr-1.3C, etc. [2-2] Titanium block shape titanium block The shape of 2 is preferably a plate shape or a column shape. The thickness of the plate-shaped titanium block 2 is 7 to 80 mm. The upper limit of the thickness may be 70 mm, 60 mm, 50 mm or 40 mm. The columnar titanium block 2 is perpendicular to the length. The shape of the cross section in the direction is a case of a circle and a polygon of a pentagon or more. When the cross-sectional shape is a circle, the diameter of the section is set to 10 to 80 mm. The upper limit of the diameter of the section may be 70 mm, 60 mm, 50mm or 40mm. In the case of polygons, the equivalent circle diameter is set to 10~80mm. The upper limit of the equivalent circle diameter can be 70mm, 60mm, 50mm or 40mm. Furthermore, the equivalent circle diameter refers to the circle equivalent to the cross-sectional area. [0083] The width of the plate-shaped titanium block 2 is not particularly limited. However, the lower limit may be equal to or equal to 100 mm. The upper limit may be 100 mm, 500 mm, 1000 mm, 2000 mm. The length of the titanium block 2 is not required. Special regulations. However, the lower limit may be the same as the plate width, the diameter or the equivalent circle diameter or 100 mm. The upper limit can be 500 mm, 1000 mm, 3000 mm, 5000 mm, 10000 mm. Since the titanium agglomerate 1 has the void 1d, the volume of the titanium block 2 made of the titanium agglomerate 1 is smaller than that of the titanium agglomerate 1. Therefore, in order to obtain the titanium block 2 of a desired size, the size of the titanium agglomerate 1 must be determined in consideration of the bulk specific gravity of the titanium agglomerate 1. For example, in order to obtain a rectangular parallelepiped titanium block 2 having a thickness of 50 mm (volume specific gravity: 4.5), a titanium agglomerate 1 having a rectangular parallelepiped shape of 70 mm (volume specific gravity: 3.2) may be prepared. Further, in order to obtain a cylindrical titanium piece 2 having a diameter of 50 mm (volume specific gravity: 4.5), a cylindrical titanium agglomerate 1 (volume specific gravity: 3.1) having a diameter of 60 mm may be prepared. When the titanium block 2 has a plate shape and the thickness thereof is less than 7 mm, the thickness of the titanium agglomerate 1 is also thin and the strength is small. At this time, when the titanium agglomerate 1 is moved or reversed, it may be broken or notched. On the other hand, when the thickness is more than 80 mm, it is necessary to make the melting depth of the titanium agglomerate 1 large in the manufacturing step of the titanium block described later. At this time, the cooling rate after melting becomes slow, and the crystal grains become large. Further, similarly to the conventional melting step, it is necessary to have an electron beam that is greatly output. When the titanium block 2 has a column shape and its diameter (the circle-equivalent diameter in the case of a polygonal prism shape) is less than 10 mm, the diameter of the titanium agglomerate 1 is also small, and the strength is small. At this time, the titanium agglomerate 1 is broken or broken when it is moved or rotated. On the other hand, when the diameter (the circle-equivalent diameter in the case of the polygonal prism shape) is more than 80 mm, the melting depth of the titanium agglomerate 1 must be made large in the manufacturing step of the titanium block to be described later. At this time, the subsequent cooling rate becomes slow, and the crystal grains become large. Further, similarly to the conventional melting step, it is necessary to have an electron beam that is greatly output. (2-3) Size of Crystal Grain of Titanium Block The titanium block 2 has a plate shape, and when the thickness is 7 to 80 mm, as shown in FIG. 2, the metal structure of the titanium block 2 is oriented from the surface of the titanium block 2 Columnar structures 2a, 2b extending in the thickness direction. The central portion in the width direction and the longitudinal direction of the titanium block 2 and the central portion in the thickness direction (the region indicated by the symbol A in Fig. 2 is hereinafter referred to as a central region. Further, the central region is located at the central portion in the thickness direction). The round equivalent average crystal grain size is 10 mm or less and is less than or equal to half the thickness of the titanium block 2. The titanium block 2 has a circular cylindrical shape having a diameter of 10 to 80 mm, or a polygonal shape having a polygonal shape of a pentagon or more and a circular equivalent diameter (a diameter of a circle having the same cross-sectional area as the cross-sectional area of the polygonal shape) of 10 to 80 mm. As shown in Fig. 3, the columnar structure 30a extends from the surface toward the center-facing direction (diameter direction) in a section perpendicular to the longitudinal direction of the titanium block 2. The circle-equivalent average crystal grain size in the central portion of the longitudinal direction and the center position of the cross section (the region indicated by the symbol C in the drawing, hereinafter referred to as the central region) is 10 mm or less, and is half the cross-sectional diameter of the titanium block 2. the following. Thereby, even when the titanium block 2 is hot-worked, even if the processing rate is small, the crystal grains can be easily separated, and the fine particles which are necessary for the product can be obtained. [0089] Further, the titanium block which is irradiated with an electron beam on the surface of the titanium agglomerate is rapidly solidified upon stopping the irradiation, and is rapidly cooled from the surface. Therefore, the cross section perpendicular to the longitudinal direction of the titanium block 2 is a crystal grain extending in a columnar shape from the surface in the vertical direction of the surface. The thickness of the titanium block (plate shape) is thinner than the conventional ingot (usually 200 to 400 mm), which is 7 to 80 mm, so that the central portion of the titanium block is also rapidly cooled. Therefore, the average crystal grain size in the central region is 10 mm or less in terms of the circle-equivalent diameter and is one-half or less in thickness. Similarly, the diameter of the titanium block (columnar) is shorter than that of the conventional ingot, which is 7 to 80 mm, so that the central portion of the titanium block is rapidly cooled. Thereby, when the titanium block 2 is thermally processed, the crystal grains can be easily separated even at a small processing rate, and the fine particles necessary for the product can be obtained. [0090] In FIG. 2, the length of the columnar structure extending from the front side and the back side is substantially the same. In other words, the length of the crystal extending from the front side and the back side to the columnar shape is substantially the same. However, the length of the columnar structure from the front side and the length of the columnar structure from the back side can be changed by increasing the output of the electron beam irradiated from the front side and the back side. At this time, since the cooling rate in the vicinity of the center of the plate thickness is also fast, the average crystal grain in the central region is 10 mm or less in terms of a circle-equivalent diameter, and is one-half or less in thickness. In Fig. 3, although the length of the columnar structure extending from the cylindrical surface is the same, the lengths are not necessarily the same. At this time, since the cooling rate in the vicinity of the center region is also fast, the average crystal grain in the central region of the cylinder is 10 mm or less in terms of the circle-equivalent diameter, and is one-half or less in diameter. Further, in Fig. 2, as a result of irradiating the side surface toward the plate width direction, the columnar structure of the short length extends from the side surface in the plate width direction. Although the irradiation of the electron beam on such a side is preferable, as long as all the titanium agglomerates 1 can be melted, it is not necessary to irradiate the electron beam on the side surface. The lower limit of the circle-equivalent diameter of the average crystal grain is not particularly limited. However, in order to make the crystal grain size small in the titanium block 2, the thickness of the titanium block 2 must be extremely thin. However, since it is limited to the thickness of the titanium block 2 which can be manufactured, it is more desirable to be 0.5 mm or more. The crystal grains to be used herein are crystal grains of α phase in the case of industrial pure titanium or α-type titanium alloy, and crystal grains of β phase in the case of α+β two-phase titanium alloy or β-type titanium alloy. When the crystal grain is polished perpendicular to the cross section in the longitudinal direction of the titanium block 2 and then etched with fluoronitric acid, it can be visually observed or enlarged by a magnifying glass (enlarged mirror). The crystal of the central region of the titanium block (the region located at 1/2 of the thickness from the surface) was observed, and the number of crystal grains was determined. The observed area was divided by the number of crystal grains, and the average area per crystal was calculated to obtain a circle. The equivalent crystal diameter is used to calculate the average crystal grain. A circle is drawn in a region where 100 to 200 crystal grains are observed, and the area of the circle is referred to as "observation area", so that the number of crystal grains observed in the circle is "number of crystal grains". When the average crystal grain size is small and it is difficult to visually observe, photographing can be performed by optical microscopic observation, and the average crystal grain is obtained in the same manner from the photograph of the structure. Further, in the titanium block 2, a part of the titanium agglomerates is melted by an electron beam to be solidified in order, and finally the entire titanium agglomerates are melted and solidified. The range of melting is limited to the portion that illuminates the electron beam, so the amount of the titanium block (titanium agglomerate) to be melted is only a small amount. Therefore, the concentration of elements other than titanium during solidification is small, that is, solidification segregation is also small. Therefore, the elemental composition other than the added titanium can be suppressed to be small depending on the place. Further, since the titanium agglomerates which are uniformly mixed in advance are partially melted in order, there is no melting unevenness of the titanium raw material, and even if there is an accident in which the electron beam irradiation is stopped, the melting is again performed from the position, that is, Generate any problems. In this way, the compositional variation in the longitudinal direction of the slab as in the direct slab casting method can also be suppressed. That is, the composition change of the titanium block 2 in the longitudinal direction is small, and the chemical composition is uniform. The composition analysis of the titanium block 2 is carried out by taking a necessary amount of the analysis sample from the specific position of the titanium block 2 by any of the following analysis methods. JIS H 1612 (1993) Method for the determination of nitrogen in titanium and titanium alloys JIS H 1614 (1995) Method for the determination of iron in titanium and titanium alloys JIS H 1617 (1995) Method for the determination of carbon in titanium and titanium alloys JIS H 1619 (2012) Titanium and Titanium Alloys - Hydrogen Quantification Method JIS H 1620 (1995) Method for Quantifying Oxygen in Titanium and Titanium Alloys JIS H 1621 (1992) Method for Quantification of Palladium in Titanium Alloys JIS H 1622 (1998) Titanium alloy-aluminum quantitative method JIS H 1624 (2005) Titanium alloy-vanadium quantitative method JIS H 1625 (2005) Titanium alloy - 镧, 铈, 鐠 and 钕 quantitative method JIS H 1630 (1995) Titanium luminescence spectroscopic analysis Method JIS H 1631 (2008) Titanium Alloy-Fluorescence X-ray Analysis Method JIS H 1632 (2014) Titanium ICP Luminescence Spectrometry Method [0095] FIG. 6 is a schematic view showing a sample for analysis. As shown in Fig. 6, the sample for analysis is divided into two at a position (end region) of 50 mm from the front end and the rear end in the longitudinal direction of the titanium block 2, and is divided into three equal parts. The total of five places in the center of the length of the division is taken at five places. In the case of the titanium block 2, in the case of the titanium block 2 of the rectangular parallelepiped shape (flat embryo), it is taken from the surface of the center of the width direction and the surface layer 2 of the back surface, when the shape of the titanium block of the cylindrical shape (ingot) It is taken from the surface layer 2 which is symmetric about the center of the section. Further, the position of 50 mm from the front end and the rear end in the longitudinal direction is also taken from the center of the thickness center/diameter direction. In this way, the analysis sample was taken from the total of 12 places (the position in Fig. 6), and the uniformity of the chemical composition was evaluated as follows. [0096] The maximum value of the content of each element C MAX With minimum C MIN The difference ⊿C is less than 0.2C MIN Or less than 0.04%, the evaluation is uniform. For example, when the minimum value of the measured value of O is 0.04% and the maximum value is 0.05%, the difference ⊿C (=0.01%) is less than 0.04%, and thus it is evaluated as uniform. Further, when the minimum value of the measured value of O is 0.30% and the maximum value is 0.32%, the difference ⊿C (= 0.02%) is less than 0.2C. MIN (=0.060%), so the assessment is uniform. For example, when the minimum value of the measured value of O is 0.03% and the maximum value is 0.05%, the difference ⊿C (=0.02%) is less than 0.04%, and thus it is evaluated as uniform. Further, when the minimum value of the measured value of O is 0.30% and the maximum value is 0.35%, the difference ⊿C (=0.05%) is less than 0.2C. MIN (=0.060%), so the assessment is uniform. 3. Method for Producing Titanium Agglomerate Titanium agglomerate 1 is a molded body obtained by compression-molding the above-mentioned raw materials 1a and 1b and an auxiliary raw material 1c as shown in Fig. 1 . [0098] Since the titanium sponge 1a or the titanium residue 1b is in an amorphous shape, it cannot be directly used as a specific shape (a rectangular parallelepiped, a prism, a cylinder, or the like). First, the necessary sponge titanium 1a, titanium residue 1b, and auxiliary material 1c are placed in a container and mixed. An element which is more volatile than titanium is reduced in volatilization by electron beam irradiation in the subsequent stage, and therefore an element in which the amount of volatilization is considered may be added in advance. [0099] The raw material to be mixed is a metal mold having the same shape as that of the titanium agglomerate 1 of a desired size, and is subjected to a specific pressure compression process to obtain a titanium agglomerate 1. The environment during compression molding is usually atmospheric (air) at normal temperature. The mixing means is not particularly limited, and from the viewpoint of productivity and the like, it is more desirable to adopt the means described below. (a) A specific amount of the sponge titanium 1a, the titanium residue 1b, and the auxiliary material 1c are charged into the mixing container. (b) stirring in the mixing vessel to uniformly mix the sponge titanium 1a, the titanium residue 1b, and the auxiliary material 1c. In the stirring method, the mixing container is rotated in the vertical direction, rotated horizontally by 20 to 70° in the oblique direction, and the mixing container is vibrated in the vertical direction or the horizontal direction, and the stirring element is inserted into the mixing container to rotate the stirring element. (c) The stirring time varies depending on the size of the mixing container or the amount of the sponge titanium 1a, the titanium residue 1b, and the auxiliary material 1c, but it is 1 to 30 minutes. When productivity is considered, it is more desirable to determine the size or throughput of the mixing vessel in such a manner that it can be uniformly mixed in a few minutes. (d) The sponge titanium 1a, the titanium residue 1b, and the auxiliary material 1c to be mixed are put into a press mold for compression molding from a mixing container, and compression molding is performed. Thereby, the titanium sponge mass 1 in which the auxiliary raw material 1c is uniformly dispersed can be obtained. The size of the titanium agglomerate 1 may be appropriately determined depending on the size of the titanium block 2 or the size of the metal mold limited by the compression processing apparatus. 4. Method for Producing Titanium Block 2 The titanium block 2 of the present invention is obtained from the titanium agglomerate 1 produced as described above, as shown in FIG. 2 . (4-1) The environmental titanium agglomerate 1 is housed in the chamber, and the pressure in the chamber is reduced to 1 Pa or less. The inside of the titanium agglomerate 1 has a plurality of voids 1d containing air (oxygen or nitrogen). When directly fused, the titanium block 2 oxidizes, nitrites, or remains bubbles, which causes cracking or surface flaws after hot working. Therefore, the pressure is 1 Pa or less, and air is excluded from the internal space 1d of the titanium agglomerate 1. [0108] The lower limit of the pressure is not particularly limited, but in order to make the pressure in the chamber extremely small, the airtightness of the device is increased, or the vacuum exhausting machine is enhanced, and the manufacturing cost is increased, so the pressure lower limit in the chamber is increased. More than expected 1 × 10 -3 Pa. (4-2) Melting the titanium agglomerate 1 provided in the chamber under reduced pressure firstly irradiates an electron beam to the upper side surface, and is sequentially melted and solidified. In detail, a part (for example, about half) 2a in the thickness direction of the titanium agglomerate 1 is irradiated with an electron beam to be sequentially melted and solidified. The range in which the electron beam can be melted is limited, so that the irradiation direction of the electron beam is moved, or the titanium agglomerate 1 is moved, and the entire side of the titanium agglomerate 1 is irradiated with an electron beam to make a part of the thickness direction of the titanium agglomerate 1. 2a melts and solidifies. After that, the titanium agglomerate 1 is reversed, and the other surface (side surface, end surface, or back surface) is the upper side, and the remaining portion (for example, about half) 2b in the thickness direction that has not been melted and solidified is irradiated with the electron beam in the same manner. The entire region in the thickness direction of the titanium agglomerate 1 is sequentially melted and solidified to form a titanium block. Thereby, a columnar structure extending from the surface in the thickness direction can be obtained. In the case of the cylindrical titanium agglomerate 1 shown in Fig. 3, when the circumferential surface is melted, the electron beam may be irradiated while rotating around the axis of the cylinder to form a titanium block. Thereby, a columnar structure extending in a direction perpendicular to the longitudinal direction of the titanium block and extending in a direction (diameter direction) from the surface toward the center can be obtained. In this way, by rotating the titanium agglomerate during melting (inversion of the plate-like agglomerates, rotation of the cylindrical agglomerates), the titanium agglomerates can be all melted and solidified to form a titanium block. When a part 2a of the titanium agglomerate 1 in the thickness direction is melted, the electron beam is adjusted so that the entire thickness direction of the titanium agglomerate 1 or the entire diameter direction is not melted. When the entire thickness or the entire diameter direction is melted (so-called electron beam penetration), the molten titanium flows out from below the titanium agglomerate 1, and the desired shape cannot be maintained. Therefore, the melting depth of the titanium agglomerate 1 is set to be less than the plate thickness of the titanium agglomerate 1 or less than the diameter of the titanium agglomerate 1. It is generally more desirable to melt the entire titanium agglomerate 1 by melting about one-half of the thickness or diameter and inverting or rotating to melt the remaining half. Further, since the size (width or length) of the titanium agglomerate 1 is limited, when a large titanium block 2 is obtained, a plurality of titanium agglomerates 1 may be arranged side by side and melt-bonded by electron beam. Further, the air removal treatment from the void 1d and the melting treatment (including the melting after the reverse rotation) of the titanium agglomerate 1 by the electron beam are preferably carried out continuously under reduced pressure. 5. Titanium Flat 3 Next, the titanium flat metal 3 and the titanium plate 4a using the titanium block 2 of the present invention will be described. [0115] As shown in FIG. 4 or FIG. 5, the titanium squash 3 is obtained by filling the titanium blocks 2 and 20 obtained above into a container made of titanium plates 4a and 40a having the same chemical composition (bundle). In the materials 4 and 40, the joint portions of the packing materials 4 and 40 are all welded to each other to form the welded portions 5 and 50. Titanium flat embryo 3, also known as titanium billet or titanium block, according to its size or shape, is shown as a material for thermal processing (intermediate product). The titanium slab 3 of the present invention is vacuum-treated inside the titanium plate 4a, and accommodates the titanium block 2 of the present invention. [0117] As shown in FIG. 4, the titanium flat blank 3 of the present invention is a titanium flat embryo having a packing material 4 formed of a titanium plate 4a and a titanium block 2 filled in the inside of the packing material 4, and is bundled. The internal pressure of the material 4 is 10 Pa or less in terms of absolute pressure, and the titanium plate 4a is a processing material having the same chemical composition as the titanium block 2. As described above, the titanium block 2 is often manufactured in such a manner as to satisfy the chemical composition range specified in various specifications. The chemical composition of the packing material 4 is preferably the same chemical composition range as that required for the titanium block 2. That is, the same species means that the packing material 4 and the titanium block 2 are within the chemical composition range of the same specification. [0118] The titanium plate material 4a forming the packing material 4 will be described. [0119] The titanium plate member 4a is a titanium plate or a titanium tube manufactured by heat or cold plastic working such as calendering, extrusion, lifting, forging, or the like. Since the titanium plate material 4a is plastically processed, it has an advantage that the surface is smooth and the structure is fine (the crystal grains are small). (5-1) When the thickness of the packing material 4 is a rectangular parallelepiped, the thickness of the titanium plate member 4a varies depending on the size of the packaging material 4 to be produced, but is preferably 0.5 mm or more and 30 mm or less. The larger the packing material 4, the more strength or rigidity is required, so a thicker titanium plate 4a is used. When it is less than 0.5 mm, the packing material 4 is deformed during heating before hot working, or it may be broken at the initial stage of hot working, which is not preferable. When the thickness is larger than 30 mm, the ratio of the titanium plate 4a to the thickness of the titanium flat blank 3 is increased, and the filling amount of the titanium block 2 is small. Therefore, the amount of the titanium block 2 to be processed is small, and the manufacturing efficiency is poor, which is not preferable. In order to reduce the cost, the thickness of the titanium plate 4a is preferably thin, and may be 20 mm or less, 10 mm or less. In order to surely prevent breakage at the initial stage of hot working, the thickness may be 1 mm or more, 2 mm or more, or 3 mm or more. Further, the thickness of the titanium plate member 4a is desirably 3% or more and 25% or less of the thickness of the titanium flat blank 3. When the thickness of the titanium plate 4a is thinner than 3% of the thickness of the titanium flat blank 3, it is difficult to hold the titanium block 2, and it is greatly deformed upon heating before hot working, or the welded portion 5 of the packing material 4 may be broken. On the other hand, when the thickness of the titanium plate member 4a is thicker than 25% of the thickness of the titanium flat blank 3, although there is no particular manufacturing problem, the proportion of the titanium plate member 4a to the thickness of the titanium flat blank 3 is increased. Since the filling amount of the titanium block 2 is small, the amount of the titanium block 2 to be processed is small, and the manufacturing efficiency is poor, which is not preferable. [0124] Similarly, when the packing material 4 is a tube, the thickness of the titanium sheet 4a varies depending on the size of the packing material 4 to be produced, but the thickness of the tube is desirably 0.5 mm or more and 30 mm or less. Further, similarly to the case of the rectangular parallelepiped, the thickness of the titanium plate member 4a is desirably 3% or more and 25% or less of the diameter of the titanium flat blank 3. Further, as shown in FIG. 5, the titanium material 2 may be filled in the packing material 40 which is formed by bending the titanium plate material 40a into a hollow tubular shape, and the end portion of the titanium plate material 40a may be welded to form the welded portion 50 to become a titanium flat. Embryo 30. (5-2) The chemical composition packing material 4 must be of the same chemical composition as the titanium block 2. Here, the chemical composition of the same kind, specifically, means the same specification as JIS. For example, when the chemical composition of the titanium block 2 belongs to JIS1, the packing material 4 is also a chemical composition belonging to JIS. Here, the specifications required for the titanium block 2 can be confirmed by documents at the time of sale or purchase or at the time of manufacture. Moreover, this specification may also be confirmed by the marking of the surface of the titanium block 2. If necessary, it may be within ±30%, ±20%, ±15%, ±10%, ±8%, ±5% or within ±3% of the chemical composition (actual value) from the titanium block 2 . [0126] Thus, by making the chemical composition of the packing material 4 into the same chemical composition as the titanium block 2, the surface layer of the processed titanium flat embryo can be made into the same chemical composition as the inside, and can be directly operated as a titanium block. . (5-3) Size of Crystal Grain of the Packing Material 4 The titanium plate material 4a can be subjected to heat treatment by moderate plastic working to adjust the crystal grains. The average crystal grain of the titanium plate material 4a used for the packing material 4 has a desired equivalent circle diameter of 500 μm or less. Thereby, when the titanium flat embryo 3 is thermally processed, the surface flaw caused by the difference in the crystal orientation of the large crystal can be suppressed. The lower limit of the circle-equivalent diameter of the average crystal grain is not particularly limited. However, in order to make the crystal grain size extremely small in the titanium plate member 4a, it is necessary to make the processing ratio in the plastic working process large, since it can be used as the packing material 4. The thickness of the titanium plate 4a is limited, so it is more desirably 10 μm or more, and more desirably more than 15 μm. The crystal particles to be used herein are crystal grains of the α phase in the case of industrial pure titanium or α-type titanium alloy, and crystal grains of the β phase in the case of the β-type titanium alloy. In the case of the α+β two-phase titanium alloy, it is a collection structure of the α phase (α sheet, α colony). The alpha sheet is an aggregate of alpha crystal grains of the same crystal orientation. [0130] The average crystal grain of the industrial pure titanium, the α-type titanium alloy, and the β-type titanium alloy is a photomicrograph of the cross-sectional structure including the thickness direction of the titanium plate material 4a constituting the packing material 4 by an optical microscope. In the photograph of the structure, the average crystal grain of the surface layer (the region from the surface to the depth of 0.3 mm) of the titanium plate material 4a was obtained by the cutting method according to JIS G 0551 (2005). The average crystal grain size (the size of the α sheet) of the α + β two-phase titanium alloy was determined by the following method using EBSD (Electron Backscatter Diffraction). First, a test piece having a cross section in the thickness direction of the packing material 4 composed of the titanium plate material 4a is taken as the observation surface, and then the surface layer of the observation surface of the test piece (from the surface to the depth of 0.3 mm) In the region, a rectangular region having a length of 2.4 mm and a width of 1.8 mm was used as a field of view, and the measurement interval was 2.3 μm, and the acceleration voltage was 15 kV, which was measured by EBSD. From the obtained measurement results, the PQ (pattern quality) pattern and the phase diagram were prepared by analyzing the Kikuchi pattern, and the α phase was extracted. Furthermore, the Kikuchi pattern analysis excludes the β phase only for the α phase. Next, the angle difference between the crystal orientations of the adjacent EBSD measurement points was 15° or less, the α sheet layer was determined, and the area of each α sheet layer was determined from the number of measurement points of the α sheet layer, and the circle equivalent diameter was calculated. [0133] Next, the titanium flat embryo 3 will be described. (5-4) The shape of the shape titanium flat embryo 3 is not limited and is determined depending on the shape of the titanium block to be produced. When a titanium thin plate is produced, the titanium flat embryo 3 has a rectangular parallelepiped shape (flat embryo). The thickness, width and length of the titanium flat blank 3 are determined depending on the thickness, width and length of the product, the amount of manufacture (weight), and the like. [0135] When a titanium round bar, a wire or an extruded profile is produced, the titanium flat blank 3 has a polygonal prism shape (binder) such as a cylindrical shape or an octagonal prism. The size (diameter, length) is determined by the thickness, width and length of the product, the amount of manufacture (weight), and the like. (5-5) The inside of the titanium squash 3 is filled with a titanium block 2 inside. The titanium block 2 can be filled in one or a plurality. A gap 6 is formed between the titanium block 2 and the packing material 4 or between the titanium blocks 2. When there is air in the gap 6, when it is heated before hot working, the filled titanium block 2 is oxidized or nitrided, and the titanium material obtained by the subsequent processing becomes brittle, and the necessary material properties cannot be obtained. Further, when an inert gas such as Ar gas is filled, oxidation or nitridation of the titanium block 2 or the package body 6 can be suppressed. However, when heated, the Ar gas thermally expands to squeeze the packing material 4, and the titanium flat embryo 3 Deformation, hot processing is not possible. [0138] For the above reasons, the gap between the titanium block 2 and the packing material 4 or between the titanium blocks 2 must be decompressed as much as possible. Specifically, the absolute pressure is desirably 10 Pa or less, and more desirably 1 Pa or less. [0139] When the internal pressure of the packing material 4 is greater than 10 Pa, the titanium block 2 or the packing material 4 is oxidized or nitrided due to the remaining air. The lower limit is not particularly limited. However, in order to make the internal pressure extremely small, the manufacturing cost increases due to the improvement of the airtightness of the device or the vacuum evacuation machine, so the lower limit of the internal pressure is expected to be 1 × 10 -3 Pa. Further, the internal pressure of the produced titanium squash 3 can be measured as follows. That is, the titanium flat blank 3 can be opened in water or in a vacuum chamber, and the total amount of gas (air) remaining inside can be recovered, the volume thereof can be measured, or the volume can be calculated based on the change in the degree of vacuum. Further, by recovering the volume of the water invading the inside, it is also possible to grasp the volume of the void in the titanium flat blank 3. According to this method, at least the internal pressure of the titanium slab 3 is 10 Pa or less. (5-6) Decompression Method Next, a method of decompressing the inside of the packing material 4 to maintain a vacuum will be described. [0142] The packing material 4 is a container which is filled with a titanium block 2 and then decompressed to a specific internal pressure or less and sealed. Alternatively, the titanium sheets 4a may be partially joined to each other, and then decompressed and sealed. By sealing, air does not intrude, and the titanium block 2 or the packing material 4 inside is not oxidized when heated before hot working. The sealing method is not particularly limited, and it is preferable that the titanium plate members 4a are welded to each other and sealed. At this time, the welded portion 5 is formed by integrally welding the joint portions of the titanium plate member 4a, that is, the entire circumference is welded. The method of welding the titanium plate 4a is not particularly limited, such as arc welding, electron beam welding, or laser welding, such as TIG welding or MIG welding. [0144] The welding environment is such that the inner faces of the titanium block 2 and the packing material 4 are not oxidized or nitrided, and are welded under reduced pressure or in an inert gas atmosphere. When the connection portion of the titanium plate member 4a is finally welded, it is more desirable to weld the packaging material 4 to a container (chamber) under reduced pressure, and to maintain the inside of the packaging material 4 in a reduced pressure state. [0145] In addition, a pipe may be provided in a part of the packing material 4 in advance, and after welding in the inert gas atmosphere, the pressure may be reduced to a specific internal pressure by the pipe, and the pipe may be sealed by pressure bonding or the like to make the pipe bundle. The inside of the bag material 4 is in a reduced pressure state. Further, at this time, the piping may be placed at a position on the rear end surface as long as it is in a position where the thermal processing does not cause a defective state in the subsequent step. (5-7) The titanium block 2 or the titanium slab 3 which is obtained by the above-described thinner or finer diameter than the conventional one is subjected to hot working or cold working to have a desired shape. Although the processing method differs depending on the shape of the titanium flat embryo, since it is thin or thin, it can be easily processed to a desired size. [0147] When a titanium plate is produced, the titanium block 2 or the titanium flat piece 3 having a rectangular parallelepiped shape (flat embryo) is heated and hot rolled to form a titanium plate. If necessary, the oxide layer may be removed by pickling or the like as in the conventional step, and then cold rolled to be thinner. [0148] When manufacturing a titanium round bar or wire, the titanium block or the titanium slab 3 of the cylindrical or polygonal prism shape is heated, hot forged, hot rolled or hot pressed to form a titanium round bar or wire. Further, if necessary, the oxide layer may be removed by pickling or the like in the same manner as in the conventional step, and then cold rolling or the like may be performed to make the film finer. In the case of producing a titanium extruded profile, a titanium block or a titanium slab 3 of a cylindrical or polygonal prism shape is heated and hot pressed to form a titanium profile of various cross-sectional shapes. [0149] When the titanium block 2 is used, there may be a case where a defect is generated on the surface of the plate or the round bar or the profile after the hot working. At this time, the surface is removed by cutting, pickling, or the like. [0150] When the titanium flat embryo 3 is used, the surface of the plate or round bar and the profile after the hot working is good, and the surface is not required to be treated. [Embodiment 1] Next, an embodiment of the present invention will be described. As a titanium source of the raw material, sponge titanium (particle size = 0.25 mm or more and 19 mm or less) manufactured by the Kroll process is used, and the oxygen content is 0.03%, the iron content is 0.02%, the nitrogen content is 0.002%, and the carbon content is 0.001%. The hydrogen content is 0.001%. Further, as a part of the titanium residue (see No. 11 and 12 in Table 1), JIS was used (the oxygen content was 0.04%, the iron content was 0.03%, the nitrogen content was 0.001%, the carbon content was 0.003%, and the hydrogen content was 0.007%). The thin plate is cut into 20~30mm square. [0153] As the auxiliary material, titanium oxide powder, electrolytic iron, Pd powder, Al particles, Al-V alloy particles, Sn particles, Zr particles, Mo powder, Ta powder, Nb are suitably used depending on the target chemical composition of the titanium block. Powder, Si powder, Cr grain, Co grain, Ni grain, Ru powder, Mm (fine alloy) powder, FeN powder, C powder, TiB 2 powder. Further, the Al-V alloy particles are an alloy having an Al content of 30% and a V content of 70%. The Mm system uses a mixture mainly composed of La (镧), Ce (铈), and Nd (钕). [0154] The titanium sponge, the titanium residue, or the auxiliary material are placed in a mixing container made of stainless steel, and the mixing container is rotated in the vertical direction to mix the raw materials. The titanium agglomerate having a rectangular parallelepiped shape is produced by putting the mixed raw material into a specific amount in an angular metal mold and compression-molding. At this time, the void ratio determined from the size and weight of the titanium agglomerate was 28 to 45%. [0155] The obtained titanium agglomerate is placed in a vacuum chamber, and the upper side of the titanium agglomerate is further fused by half of the thickness of the titanium agglomerate by electron beam to 2 to 3 mm. The amount (thickness) of the melting is determined in advance by the relationship between the output of the electron beam and the thickness of the meltable, and as a result, the output of the electron beam is obtained from the necessary thickness. After solidifying and cooling the upper side of the titanium agglomerate, the titanium agglomerates were reversed, and the back surface was similarly melted. [0156] In this manner, the entire titanium agglomerates were melted and solidified, and a rectangular parallelepiped titanium block having various thicknesses of 300 mm and a length of 1200 mm was produced. A titanium block in which only the vicinity of the surface layer of the titanium block was melted and the raw material was not melted inside was also produced as a comparative example (see Tables No. 25 and 26). In all cases, the thickness of the melted surface layer is 4 to 8 mm on each side. [0158] A part of the obtained titanium block was cut to carry out component analysis, and the homogeneity thereof was evaluated. The remaining titanium block is hot rolled to a rolled plate having a thickness of 3.5 to 8.0 mm. [0159] As a conventional example, a titanium ingot is obtained by using an EB melting furnace having a cold hearth. That is, titanium sponge, titanium oxide, electrolytic iron, and Al particles are used as raw materials to be put into a cold hearth, an electron beam is irradiated to the raw material, and molten titanium is injected into a mold having a thickness of 250 mm to obtain a titanium ingot. In the initial stage of melting, the melting rate was started at 0.35 ton/h, and the melting rate was gradually increased, and the constant portion was melted at 0.75 ton/h. Thereafter, the melting rate was gradually lowered, and after the end of the melting down to 0.2 ton/h, the melting was terminated to obtain a titanium ingot having a length of 1200 mm. The crystal grain size of the central portion of the titanium block was measured visually or using a metal microscope. Further, the composition analysis of the titanium block is carried out by taking a necessary amount of the analysis sample from a specific position of the titanium block by any of the following analysis methods. JIS H 1612 (1993) Method for the determination of nitrogen in titanium and titanium alloys JIS H 1614 (1995) Method for the determination of iron in titanium and titanium alloys JIS H 1617 (1995) Method for the determination of carbon in titanium and titanium alloys JIS H 1619 (2012) Titanium and Titanium Alloys - Hydrogen Quantification Method JIS H 1620 (1995) Method for Quantifying Oxygen in Titanium and Titanium Alloys JIS H 1621 (1992) Method for Quantification of Palladium in Titanium Alloys JIS H 1622 (1998) Titanium alloy-aluminum quantitative method JIS H 1624 (2005) Titanium alloy-vanadium quantitative method JIS H 1625 (2005) Titanium alloy - 镧, 铈, 鐠 and 钕 quantitative method JIS H 1630 (1995) Titanium luminescence spectroscopic analysis Method JIS H 1631 (2008) Titanium alloy-fluorescent X-ray analysis method JIS H 1632 (2014) Titanium ICP emission spectroscopic analysis method [0161] 50 mm from the front end and the rear end of the length of the titanium block 2 Two of the positions (end regions) were taken at a total of five places at the center of three equal divisions and each of the equal lengths, and were taken as samples for analysis. In the case of the titanium block 2, in the case of the titanium block 2 of the rectangular parallelepiped shape (flat embryo), it is taken at the surface of the center in the width direction and at the surface layer 2 of the back surface, in the case of a titanium block of a cylindrical shape (ingot) It is taken from the surface layer 2 which is symmetric about the center of the section. Further, the position of 50 mm from the front end and the rear end in the longitudinal direction is also taken from the center of the thickness center/diameter direction. In this way, the analysis sample was taken for analysis from the total of 12 (the position of ● in Fig. 6), and the uniformity of the chemical composition was evaluated as follows. The maximum value of the content of each element C MAX With minimum C MIN The difference ⊿C, when it is less than 0.2C MIN Or less than 0.04%, the evaluation was good. For example, when the minimum value of the measured value of O is 0.04% and the maximum value is 0.05%, the difference ⊿C (=0.01%) is less than 0.04%, and therefore it is evaluated that the uniformity is good. Further, when the minimum value of the measured value of O is 0.30% and the maximum value is 0.32%, the difference ⊿C (= 0.02%) is less than 0.2C. MIN (=0.060%), so the evaluation was good. Further, the crystal grain size at the center of the thickness was measured by a visual or metal microscope at a position of 50 mm from the front end and the rear end in the longitudinal direction, and the average value thereof was determined. The remaining titanium block is hot rolled to a plate having a thickness of 3.5 mm to 8 mm. In the first embodiment, the production conditions of the titanium block are summarized in Table 2. The titanium blocks produced in Table 2 are summarized in Table 3, and the titanium material (rolled sheet) produced by rolling the titanium block is summarized in Table 4. [0165] [0166] [0167] [0168] As shown in Tables 2 to 4, Nos. 1 to 8 are those in which the thickness and the void ratio of the titanium agglomerate are changed, and the titanium block is produced in various thicknesses. [0169] No. 1, when the thickness of the titanium agglomerate is as thin as 8 mm, a thin titanium block having a thickness of 5.7 mm can be obtained, but the corner of one portion of the titanium agglomerate is defective, so that it cannot be rolled. [0170] Other than the thickness No. 2 to 8, the chemical composition is homogeneous, and the crystal grain size at the center of the thickness of the titanium block is as small as 0.8 to 7.8 mm, and the rolling can be performed without problems, and a part of the surface of the rolled plate Although surface flaws occur, they are generally good. The surface generated by a portion can be partially processed and removed. [0171] No. 8 to 10 are the case of producing a JIS type, a JIS type, and a JIS type of a rolled sheet, and No. 11 and 12 are a part or all of the JIS type 1 titanium chips, and the JIS type 2 and the JIS type 3 are produced. The case of a rolled plate. In all of the cases, the composition is homogeneous, and the titanium block having a small crystal grain size at the center can be obtained, and the subsequent rolling can be carried out without problems. A part of the surface of the rolled plate has a surface flaw but is generally good. No. 13 to 24 are cases in which various metal elements other than Fe and Fe are added as an auxiliary material. In all of these cases, the composition is homogeneous, and the titanium block having a small crystal grain size in the center can be obtained, and the subsequent rolling can be carried out without problems. A part of the surface of the rolled plate has a surface flaw but is generally good. In Nos. 25 and 26 of the comparative example, a titanium block in which the vicinity of the surface layer of the titanium agglomerate was melted and the raw material (sponge titanium, auxiliary material) was not melted and left directly was produced. Since the center portion of the thickness of the titanium block is not melted, the center portions of the two positions (end regions) of 50 mm from the front end and the rear end in the longitudinal direction are maintained as titanium agglomerates. Therefore, the analysis of the center portion and the measurement of the crystal grain size cannot be performed, and therefore the description is omitted. That is, the analysis was to evaluate the uniformity of the chemical composition from the 10 sites taken from the surface portion of the self-melting titanium block. [0175] In such a titanium block, an additive element other than titanium such as oxygen or Fe greatly changes depending on the position of the titanium block, and becomes an inhomogeneous ingot. Further, after the ingot is rolled, the deformation resistance at a high temperature greatly differs depending on the inhomogeneity of the ingot, and thus a large surface crack is generated. Therefore, it cannot be used as an article. Further, in all of the comparative examples of No. 1 to No. 26 and the examples of the present invention, the content of titanium is 70% or more. Further, carbon, nitrogen or hydrogen contained as impurities in the sponge titanium or titanium residue is contained in all of the comparative examples and the present invention examples. In the conventional example, No. 27 is a result of melting the industrial pure titanium (JIS type 2) by a conventional method, and the flat germline is larger than 250 mm. Therefore, the segregation of the Fe component is large, and the thickness of the Fe component is large. The crystal grains are also 13 mm larger. Further, the calendered sheet produces a large amount of a flawed surface flaw. No. 28 is a result of melting the Ti-5Al-1Fe alloy, and the flat germline is large by 250 mm. Therefore, the segregation of the Fe component is large, and the variation of the Fe component is large, and the crystal grain at the center of the thickness is also 12 mm. Further, the variation of the Al composition is large due to the variation in the amount of Al volatilization. Further, the calendered sheet produces a large amount of braided surface flaws. [Example 2] A titanium block having a thickness of 35 mm, a width of 300 mm, and a length of 400 mm, which was produced in the same manner as in No. 4 of Example 1, was used to produce a titanium flat embryo. [0179] The titanium packing material is the same JIS 2 material as the titanium block having a thickness of 1 to 20 mm. In the titanium packing material which is a side surface of the container which is not in contact with the calender roll when rolling the titanium flat blank, the pipe having the valve is fixed by the tungsten gas in a gas-blunt manner. The piping of the piping is closed. The five titanium packing materials including the titanium packing material to which the piping was welded were temporarily assembled as a container, and the titanium block was accommodated therein, and the remaining titanium packing material was capped. The temporarily assembled package body is placed in a vacuum chamber, and after decompression (vacuum) to a specific pressure, the connection portion of the packaging material is welded by a full-circumferential electron beam to prepare a titanium flat embryo (refer to No. 2 of Table 5). 3, 5). A vacuum gauge was placed on the piping on the side of the fabricated titanium slab, and the valve was opened to measure the internal pressure. After the measurement, the pipe was sealed between the titanium slab and the valve, and the valve was cut and removed. [0180] After the titanium flat embryo is assembled by tungsten gas fusion, the exhaust pipe is placed under the exhaust pipe provided in the titanium packing material, and the pressure is reduced (vacuum) to a specific pressure inside the titanium flat embryo, and then the exhaust gas is used. The piping is sealed to adjust the internal pressure of the titanium flat embryo. [0181] These titanium flat embryos having a thickness of 37 to 75 mm are rolled to prepare a rolled sheet having a thickness of 4.0 to 5.5 mm. The results of Example 2 are summarized in Table 5 together with the test conditions. [0183] As shown in Table 5, No. 1 to 3 in which the internal pressure of the titanium slab was 10 Pa or less was rolled without problems, and the surface of the obtained rolled sheet was also good. [0185] No. 4 in which the internal pressure of the titanium slab was 12 Pa was rolled without any problem, but a part of the obtained rolled plate was cleaved into two pieces and peeled off. When the peeled portion was observed, it was found that the surface of the titanium block and the titanium packing material was oxidized, and the two materials were not crimped. [0186] Similarly, a titanium block produced in the same manner as in No. 14 of Example 1 was used to produce a titanium flat embryo. [0187] The titanium packing material was the same Ti-5Al-1Fe material (number in mass %) as the titanium block having a thickness of 10 mm. After temporarily assembling five titanium packing materials into a container, the titanium block was accommodated therein, and the remaining titanium packing material was capped. [0188] The temporarily assembled package body was placed in a vacuum chamber, and after decompression (vacuum) to a specific pressure, the connection portion of the packaging material was welded by a full-circumferential electron beam to prepare a titanium flat embryo (No. 5). [0189] The titanium flat blank was rolled to prepare a rolled sheet having a thickness of 5.0 mm. Calendering can be carried out without problems, and the surface of the obtained rolled sheet is also good. [Example 3] As a titanium source as a raw material, sponge titanium (particle size = 0.25 mm or more and 19 mm or less) manufactured by the Kroll process was used, and the oxygen content was 0.04%, the iron content was 0.03%, and the nitrogen content was 0.003%. The carbon content is 0.003% and the hydrogen content is 0.001%. Further, as a part of the titanium residue (see No. 10 and 11 in Table 3), JIS was used (the oxygen content was 0.04%, the iron content was 0.03%, the nitrogen content was 0.003%, the carbon content was 0.004%, and the hydrogen content was 0.003%). The thin plate is cut into 20~30mm square. [0191] As the auxiliary material, titanium oxide powder, electrolytic iron, Pd powder, Al particles, Al-V alloy particles, Sn particles, Zr particles, Mo powder, Ta powder, Nb powder are suitably used depending on the target component of the titanium block. , Si powder, Cr grain, Co grain, Ni grain, Ru powder, Mm (fine alloy) powder, FeN powder, C powder, TiB 2 powder. Further, the Al-V alloy particles are an alloy having an Al content of 30% and a V content of 70%. [0192] The titanium sponge, the titanium residue, or the auxiliary material are placed in a mixing container made of stainless steel, and the mixing container is rotated in the vertical direction to mix the raw materials. The mixed raw materials were placed in a specific amount in a cylindrical metal mold and compression-molded to prepare three cylindrical titanium agglomerates (length 300 mm). At this time, the void ratio determined from the size and weight of the titanium agglomerate was 28 to 40%. [0193] The obtained titanium agglomerates were placed side by side in the longitudinal direction and placed in a vacuum chamber, and the peripheral surface of the titanium agglomerates was melted by electron beam to form one half of the titanium agglomerate by more than 2 to 3 mm. The amount (diameter) of the melting is determined in advance by the relationship between the output of the electron beam and the thickness of the meltable, and as a result, the output of the electron beam is obtained from the necessary thickness. The entire circumference is melted and solidified while rotating the titanium agglomerates. [0194] In this manner, the entire titanium agglomerates were melted and solidified to prepare a columnar titanium block having a length of 900 mm and a diameter of 9 to 78 mm. The uniformity of the chemical composition and the crystal grain size were evaluated in the same manner as in Example 1. [0195] As a conventional example, a titanium ingot is obtained by using an EB melting furnace having a cold hearth. That is, titanium sponge, titanium oxide, electrolytic iron, and Al particles were used as raw materials, and they were put into a cold hearth, an electron beam was irradiated to the raw material, and molten titanium was injected into a mold having a diameter of 600 mm. In the initial stage of melting, the melting rate was started at 0.5 ton/h, and the melting rate was gradually increased, and the constant portion was melted at 0.85 ton/h. Thereafter, the melting rate was gradually lowered, and after the end of the melting down to 0.3 ton/h, the melting was terminated to obtain a titanium ingot having a length of 900 mm. The titanium ingot was subjected to an analysis sample and a tissue observation sample, and then forged to φ100 mm, and further rolled to obtain a round bar of φ30 mm. In the third embodiment, the production conditions of the titanium block are summarized in Table 6, the titanium blocks produced are summarized in Table 7, and the titanium materials (round bars) produced by rolling the titanium block are summarized in Table 8. [0197] [0198] [0199] As shown in Tables 6 to 8, as a comparative example, a titanium block in which only the vicinity of the surface layer of the titanium block was melted and the raw material was not melted inside was produced in No. 22. In the same manner as in Example 1, the obtained titanium block was subjected to chemical composition analysis in the same manner as in Example 1, and its homogeneity was evaluated by the same method as in Example 1. Further, the crystal grain size perpendicular to the central portion of the cross section in the longitudinal direction was measured by a visual or metal microscope at the central portion in the longitudinal direction. The remaining titanium block is hot rolled into a round bar having a diameter of 8 mm to 18 mm. Nos. 1 to 6 in Tables 6 to 8 are cases in which the diameter and the porosity of the titanium agglomerate were changed to prepare titanium blocks of various diameters. When the diameter of the titanium agglomerate is as thin as 11 mm, a titanium block having a diameter of 9 mm can be obtained, but one of the titanium agglomerates is partially broken, so that it cannot be calendered (No. 1). The titanium block of the other diameter can be rolled without problems, and a good round bar (No. 2 to 6) can be obtained. No. 7 to 9 are in the case of producing a titanium block of JIS type 1 , JIS type 3, and JIS type 4, and some or all of JIS 1 type titanium chips are used in No. 10 and 11 to produce JIS type 2 and JIS 3 types. The case of a rolled plate. In all of these cases, the chemical composition has a small variation in chemical composition, and a titanium block having a small crystal grain size in the center can be obtained, and the subsequent rolling is not problematic, and a good round bar can be obtained. [0204] No. 12 to 21 are cases in which various metal elements other than Fe and Fe are added as an auxiliary material. In all of these cases, the composition is homogeneous, and the titanium block having a small crystal grain size in the center can be obtained, and the subsequent rolling can be carried out without problems, and a good round bar can be produced. In No. 22 of the comparative example, a titanium block having a diameter of 44 mm which was directly deposited in the vicinity of the surface layer of the titanium agglomerate and which was not melted by the raw material (sponge titanium and the auxiliary material) was produced. Since the center portion of the thickness of the titanium block is not melted, the center portion at two positions (end regions) of 50 mm from the front end and the rear end in the longitudinal direction is maintained as a titanium agglomerate. Therefore, the analysis of the center portion and the measurement of the crystal grain size cannot be performed, and therefore will be omitted. That is, the analysis evaluates the uniformity of the chemical composition from the 10 sites taken from the surface portion of the self-melting titanium block. [0206] After analyzing the chemical composition of the titanium block, oxygen or Fe added as an auxiliary material greatly changes depending on the position of the titanium block, and becomes an inhomogeneous ingot. Further, after the ingot is rolled, the deformation resistance at a high temperature greatly differs depending on the heterogeneity of the chemical composition, so that a large amount of surface cracking occurs. Therefore, it cannot be used as an article. Further, in all of the comparative examples of No. 1 to No. 22 and the examples of the present invention, the content of titanium is 70% or more. Further, carbon, nitrogen or hydrogen contained as impurities in the sponge titanium or titanium residue is contained in all of the comparative examples and the present invention examples. In the conventional example, No. 23 is a result of melting the industrial pure titanium (JIS type 2) by a conventional method, and the ingot block diameter is 600 mm, which is large. Therefore, the solid content segregation is large, and the variation of the Fe composition is large, and the thickness is large. The crystal grains in the center are also 14 mm larger. Further, since a large amount of surface cracking occurs during forging, it is necessary to remove the portion and the manufacturing yield is greatly lowered. No. 24 is a result of melting the Ti-6Al-4V alloy by a conventional method, and the ingot block diameter is 600 mm, which is large. Therefore, due to solidification segregation, the deviation of the Fe component is large, and the crystal grain at the center of the thickness is also 13 mm. . Further, the variation of the Al composition is large due to the variation in the amount of Al volatilization. Further, since a large amount of surface cracking occurs during forging, it is necessary to remove the portion and the manufacturing yield is greatly lowered. [Industrial Applicability] According to the present invention, the conventional melting step and the forging step can be omitted, and a titanium block having a thin or fine diameter of various chemical compositions can be produced, and can be reduced in the thermal processing of the subsequent step. The amount of processing to make titanium blocks. Therefore, the energy required for manufacturing can be reduced. Further, by forming the titanium flat blank, the cutting of the defects generated on the surface of the titanium block can be omitted, and the manufacturing yield can be greatly improved, and the manufacturing cost can be greatly reduced.

[0210][0210]

1‧‧‧鈦團塊1‧‧‧Titanium mass

1a‧‧‧海綿鈦1a‧‧‧Sponge titanium

1b‧‧‧鈦殘屑1b‧‧‧Titanium debris

1c‧‧‧副原料1c‧‧‧Subsidiary materials

1d、6‧‧‧空隙1d, 6‧‧ ‧ gap

2、20‧‧‧鈦塊2, 20‧‧‧ titanium block

2a‧‧‧厚度方向的一部分2a‧‧‧ part of the thickness direction

2b‧‧‧厚度方向之剩餘一部分2b‧‧‧The remaining part of the thickness direction

3、30‧‧‧鈦扁胚3, 30‧‧‧Titanium flat embryo

4、40‧‧‧捆包材料4, 40‧‧‧Package materials

4a‧‧‧鈦板材4a‧‧‧Titanium sheet

5、50‧‧‧熔接部5, 50‧‧‧welding

A‧‧‧中央區域A‧‧‧Central area

C‧‧‧中心區域C‧‧‧Central area

[0046] 　　[圖1]圖1為示意性顯示鈦團塊之一例之說明圖。 　　[圖2]圖2為示意性顯示鈦塊之一例之說明圖。 　　[圖3]圖3為示意性顯示鈦塊之其他例子之說明圖。 　　[圖4]圖4為示意性顯示鈦扁胚之一例之說明圖。 　　[圖5]圖5為示意性顯示鈦扁胚之其他例子之說明圖。 　　[圖6]圖6為顯示分析用試樣之示意圖。[ Fig. 1] Fig. 1 is an explanatory view schematically showing an example of a titanium agglomerate. Fig. 2 is an explanatory view schematically showing an example of a titanium block. Fig. 3 is an explanatory view schematically showing another example of a titanium block. Fig. 4 is an explanatory view schematically showing an example of a titanium flat embryo. Fig. 5 is an explanatory view schematically showing another example of a titanium flat embryo. Fig. 6 is a schematic view showing a sample for analysis.

Claims (5)

一種鈦塊，其係厚度為7~80mm之板狀之鈦塊， 　　其化學組成，以質量%計，為 　　O：0.01~0.5%、 　　Fe：0.01~5%、 　　Al：0~8%、 　　Sn：0~5%、 　　Zr：0~12%、 　　Mo：0~15%、 　　Ta：0~2%、 　　V：0~22%、 　　Nb：0~2%、 　　Si：0~1%、 　　Cr：0~10%、 　　Cu：0~0.1%、 　　Co：0~1%、 　　Ni：0~1%、 　　鉑族元素：0~0.5%、 　　REM：0~0.2%、 　　B：0~3%、 　　N：0~0.2%、 　　C：0~2%、 　　H：0~0.013%， 　　剩餘部分為鈦及雜質， 　　各元素之測定值的最大值CMAX 與最小值CMIN 之差分⊿C，為未達0.2CMIN 或未達0.04%， 　　金屬組織，為 　　前述鈦塊於厚度方向之中央部的圓當量平均結晶粒徑為10mm以下，且為前述鈦塊之厚度的一半以下。A titanium block, which is a plate-shaped titanium block having a thickness of 7 to 80 mm, and its chemical composition, in mass%, is O: 0.01 to 0.5%, Fe: 0.01 to 5%, Al: 0 to 8%, Sn : 0~5%, Zr: 0~12%, Mo: 0~15%, Ta: 0~2%, V: 0~22%, Nb: 0~2%, Si: 0~1%, Cr: 0~10%, Cu: 0~0.1%, Co: 0~1%, Ni: 0~1%, platinum group elements: 0~0.5%, REM: 0~0.2%, B: 0~3%, N :0~0.2%, C:0~2%, H:0~0.013%, the remaining part is titanium and impurities, and the difference between the maximum value C MAX and the minimum value C MIN of the measured value of each element is 未C 0.2 C MIN or less than 0.04%, the metal structure is a circle-equivalent average crystal grain size of the titanium block in the central portion in the thickness direction of 10 mm or less, and is less than or equal to half the thickness of the titanium block. 一種鈦塊，其係具有垂直於長度方向之截面為直徑10~80mm之圓形的圓柱形狀，或圓當量直徑為10~80mm之五角形以上的多角形之柱形狀的鈦塊， 　　其化學組成，以質量%計，為 　　O：0.01~0.5%、 　　Fe：0.01~5%、 　　Al：0~8%、 　　Sn：0~5%、 　　Zr：0~12%、 　　Mo：0~15%、 　　Ta：0~2%、 　　V：0~22%、 　　Nb：0~2%、 　　Si：0~1%、 　　Cr：0~10%、 　　Cu：0~0.1%、 　　Co：0~1%、 　　Ni：0~1%、 　　鉑族元素：0~0.5%、 　　REM：0~0.2%、 　　B：0~3%、 　　N：0~0.2%、 　　C：0~2%、 　　H：0~0.013%， 　　剩餘部分為鈦及雜質， 　　各元素之測定值的最大值CMAX 與最小值CMIN 之差分⊿C，為未達0.2CMIN 或未達0.04%， 　　金屬組織，為 　　於垂直於前述鈦塊之長度方向的截面，具有於由表面朝向中心之方向延伸的柱狀組織，前述截面之中心位置的圓當量平均結晶粒徑為10mm以下，且為前述截面之直徑的一半以下。A titanium block having a circular cylindrical shape with a diameter of 10 to 80 mm in a cross section perpendicular to the longitudinal direction, or a polygonal titanium column having a polygonal equivalent shape of a pentagon having an equivalent diameter of 10 to 80 mm, the chemical composition thereof, In mass%, it is O: 0.01 to 0.5%, Fe: 0.01 to 5%, Al: 0 to 8%, Sn: 0 to 5%, Zr: 0 to 12%, Mo: 0 to 15%, Ta: 0~2%, V: 0~22%, Nb: 0~2%, Si: 0~1%, Cr: 0~10%, Cu: 0~0.1%, Co: 0~1%, Ni: 0 ~1%, platinum group elements: 0~0.5%, REM: 0~0.2%, B:0~3%, N:0~0.2%, C:0~2%, H:0~0.013%, the rest For titanium and impurities, the difference between the maximum value C MAX of the measured value of each element and the minimum value C MIN is less than 0.2 C MIN or less than 0.04%, and the metal structure is perpendicular to the length of the titanium block. The cross section has a columnar structure extending from the surface toward the center, and the circle-equivalent average crystal grain size at the center of the cross section is 10 mm or less and is less than or equal to half the diameter of the cross section. 一種鈦扁胚，其具備 　　具有與如請求項1或2之鈦塊同種之化學組成的捆包材料，與 　　填充於前述捆包材料之內部的如請求項1或2之鈦塊，且 　　前述捆包材料之內壓為10Pa以下。A titanium flat embryo comprising a packing material having the same chemical composition as the titanium block of claim 1 or 2, and a titanium block as claimed in claim 1 or 2 filled in the interior of the aforementioned packing material, and the aforementioned bundle The internal pressure of the bag material is 10 Pa or less. 如請求項1或2之鈦塊之製造方法，其具備 　　將由海綿鈦及鈦殘屑中選擇之一種以上，與含有為了調整化學組成所必要之元素的副原料予以壓縮成形而得到鈦團塊之壓縮成形步驟、 　　於1Pa以下之減壓下對前述鈦團塊之表面照射電子束以將前述鈦團塊之全部熔解而成為鈦塊之熔解步驟。The method for producing a titanium block according to claim 1 or 2, which comprises one or more selected from the group consisting of sponge titanium and titanium residues, and a secondary material containing an element necessary for adjusting a chemical composition, to obtain a titanium agglomerate. In the compression molding step, an electron beam is irradiated onto the surface of the titanium agglomerate under a reduced pressure of 1 Pa or less to melt all of the titanium agglomerates to form a melting step of the titanium block. 如請求項4之鈦塊之製造方法，其中前述熔解步驟，具備對前述鈦團塊之任意表面照射電子束，由其表面起熔解厚度方向之一部分之步驟，及對任意之其他表面照射電子束，至少將未熔解之鈦團塊熔解之步驟。The method for producing a titanium block according to claim 4, wherein the melting step comprises the steps of irradiating an electron beam to any surface of the titanium agglomerate, melting a portion of the thickness direction from the surface thereof, and irradiating the electron beam to any other surface. a step of melting at least the unmelted titanium agglomerate.
TW106126534A 2017-08-07 2017-08-07 Titanium block, manufacturing method thereof, and flat titanium blank for manufacturing titanium blocks at low cost TW201910528A (en)

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Publication number Priority date Publication date Assignee Title
CN112779437A (en) * 2019-10-23 2021-05-11 大田精密工业股份有限公司 Titanium alloy material for golf club head and golf titanium alloy club head
CN112813301A (en) * 2019-11-12 2021-05-18 新疆大学 Low-cost corrosion-resistant titanium alloy and preparation method thereof
CN114480914A (en) * 2021-11-10 2022-05-13 新疆湘润新材料科技有限公司 Titanium alloy material for armor and preparation method thereof
CN114752811A (en) * 2022-03-23 2022-07-15 大连理工大学 High-aluminum high-molybdenum high-zirconium ultrahigh-strength and high-toughness titanium alloy with good additive manufacturing performance and preparation method thereof
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CN114959360B (en) * 2022-06-16 2023-01-24 昆明理工大学 Corrosion-resistant titanium alloy, preparation method thereof and corrosion-resistant flexible bearing
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