201024008 六、發明說明： 【發明所屬之技術領域】 本發明是關於鑽孔工具及其製造方法。 【先前技術】 近年來，電子機器不斷朝小型化、高速度化、高功能 化進展，對於半導體1C之高集積化及印刷配線板之高密 Φ 度構裝的要求也越來越高。因此，對於組裝在電子機器內 的印刷配線板所使用之鑽孔工具的需求也逐年擴大，現在 是以直徑0.4mm以下的鑽孔工具爲主流。 然而，例如專利文獻1所揭示之印刷配線板加工用的 鑽孔工具（鑽頭）的本體構造，基本上可分成以下3類。 (1)整塊型（solid type) 刃部和柄部是由超硬合金形成一體，由於全體都使用 高價的超硬合金，價格非常高。 φ ( 2)插入型 在不鏽鋼製的棒材設置凹部，在該凹部藉由收縮配合 (shrink fit)等來將超硬合金製的棒材插入而形成一體化 ，在超硬合金側形成刃部，在不鏽鋼側形成柄部，由於使 用較便宜的不鏽鋼，相較於整塊型的情況可降低成本，但 必須考慮超硬合金製的棒材插入時的精度而將插入部分做 得較長，或必須進行高精度的孔加工，如此仍會造成成本 變高。 (3)焊接型 -5- 201024008 在刃部和柄部之間透過焊料來將兩者接合，相較於插 入型可省略插入部分，因此能進一步減少超硬合金的使用 量，但由於必須使用焊料和化學藥品，且製造程序變多， 如此仍會導致成本變高。 〔專利文獻1〕日本特開2006-55915號公報 【發明內容】 如上所述，在印刷配線板所使用的鑽孔工具，主要是 @ 使用以碳化鎢爲主成分之超硬合金，碳化鎢是屬於稀有金 屬故價格高昂，若減少超硬合金的使用量將有助於降低製 造成本。 本發明是有鑑於上述現狀而開發完成的，其目的是爲 了提供一種非常實用的鑽孔工具及其製造方法，其不須使 用焊料和化學藥品並能減少超硬合金的使用量，可發揮充 分的接合強度、能低成本地製造且接合強度優異。201024008 VI. Description of the Invention: TECHNICAL FIELD OF THE INVENTION The present invention relates to a drilling tool and a method of manufacturing the same. [Prior Art] In recent years, electronic devices have been moving toward miniaturization, high speed, and high functionality, and the demand for high integration of semiconductor 1C and high-density Φ-degree mounting of printed wiring boards is increasing. Therefore, the demand for a drilling tool used for a printed wiring board incorporated in an electronic device has been increasing year by year, and it is now mainstreamed with a drilling tool having a diameter of 0.4 mm or less. However, for example, the body structure of a drilling tool (drill) for processing a printed wiring board disclosed in Patent Document 1 can be basically classified into the following three categories. (1) Solid type The blade and the shank are made of super-hard alloy. Since all of them are made of high-priced super-hard alloy, the price is very high. φ (2) Insert type is provided in a stainless steel rod, and a concave portion is formed in the concave portion by a shrink fit or the like, and a rod made of a super-hard alloy is inserted to form an integral portion, and a blade portion is formed on the super-hard alloy side. The shank is formed on the stainless steel side, and since the stainless steel is used, the cost can be reduced as compared with the case of the monolithic type, but the insertion portion can be made longer by considering the precision of the rod made of the super-hard alloy. Or it is necessary to perform high-precision hole processing, which still causes a high cost. (3) Weld type -5 - 201024008 The two are joined by solder between the blade and the shank. The insertion portion can be omitted compared to the insert type, so the amount of cemented carbide can be further reduced, but it must be used. Solder and chemicals, and manufacturing processes have increased, which still leads to higher costs. [Patent Document 1] Japanese Laid-Open Patent Publication No. 2006-55915. SUMMARY OF THE INVENTION As described above, the drilling tool used in the printed wiring board is mainly a @hard alloy using tungsten carbide as a main component, and tungsten carbide is It is a rare metal and is expensive. If the use of superhard alloys is reduced, it will help to reduce manufacturing costs. The present invention has been developed in view of the above circumstances, and an object thereof is to provide a very practical drilling tool and a method of manufacturing the same, which can reduce the amount of use of a superhard alloy without using solder and chemicals. The joint strength can be produced at low cost and the joint strength is excellent.
參照所附的圖式來說明本發明的要旨。 Q 鑽孔工具，是由具有刃部1之本體部2和柄部3所構 成，前述刃部1是由主成分爲碳化鎢及鈷之超硬合金構件 4所形成，前述柄部3是由不鏽鋼構件5所形成，將兩者 熔接接合而構成；該鑽孔工具的特徵在於：在前述超硬合 金構件4與前述不鏽鋼構件5的接合界面7之至少20%以 上的面積，使前述不鏽鋼構件5的鐵成分侵入前述超硬合 金構件4。 此外，鑽孔工具，是由具有刃部1之本體部2和柄部 -6- 201024008 3所構成，前述刃部1是由主成分爲碳化鎢及銘之超硬合 金構件4所形成，前述柄部3是由不鏽鋼構件5所形成’ 將兩者熔接接合而構成；該鑽孔工具的特徵在於：在前述 超硬合金構件4與前述不鏽鋼構件5的接合界面7之至少 20%以上的面積，使前述不鏽鋼構件5的鐵成分侵入前述 超硬合金構件4;該鐵成分朝前述超硬合金4的侵入深度 設定爲5 ·0〜50·0μιη。 φ 此外，鑽孔工具，是由具有刃部1之本體部2和柄部 3所構成，前述刃部1是由主成分爲碳化鎢及銘之超硬合 金構件4所形成，前述柄部3是由不鏽鋼構件5所形成’ 將兩者熔接接合而構成；該鑽孔工具的特徵在於：在前述 超硬合金構件4與前述不鏽鋼構件5的接合界面7之至少 2 0%以上的面積，使前述超硬合金構件4的鈷成分脫落。 此外，鑽孔工具，是由具有刃部1之本體部2和柄部 3所構成，前述刃部1是由主成分爲碳化鎢及鈷之超硬合 φ 金構件4所形成，前述柄部3是由不鏽鋼構件5所形成， 將兩者熔接接合而構成；該鑽孔工具的特徵在於：在前述 超硬合金構件4與前述不鏽鋼構件5的接合界面7之至少 2 0%以上的面積，使前述超硬合金構件4的鈷成分脫落， 且從前述接合养面7起算，該鈷成分的脫落深度設定爲 5.0~5 0 · 0 μιη。 此外，在請求項1記載的鑽孔工具中，前述超硬合金 構件4和前述不鏽鋼構件5是藉由電阻熔接進行接合。 此外’在請求項2記載的鑽孔工具中，前述超硬合金 201024008 構件4和前述不鏽鋼構件5是藉由電阻熔接進行接合。 此外’在請求項3記載的鑽孔工具中，前述超硬合金 構件4和前述不鏽鋼構件5是藉由電阻熔接進行接合。 此外’在請求項4記載的鑽孔工具中，前述超硬合金 構件4和前述不鏽鋼構件5是藉由電阻熔接進行接合。 另外，在請求項1〜8中任一項記載的鑽孔工具中，包 含前述接合界面7之前述超硬合金構件4與前述不鏽鋼構 件5的接合部6，是設置在比前述本體部2與前述柄部3 φ 的邊界更接近前述本體部2側的位置。 此外’在請求項9記載的鑽孔工具中，前述接合部6 是設置在：從前述本體部2與前述柄部3的邊界起算朝前 述本體部2的前端5_0mm以下的範圍內。 此外，在請求項10記載的鑽孔工具中，前述本體部2 的長度設定爲5.0〜7.0mm。 此外，在請求項11記載的鑽孔工具中，前述超硬合 金構件4之與前述不鏽鋼構件5接觸的基端部的直徑設定 _ 爲 0.6〜l_4mm。 此外’在請求項12記載的鑽孔工具中，前述刃部1 的直徑設定爲〇.4mm以下。 此外’在請求項13記載的鑽孔工具中，在前述刃部1 的外周形成切削屑排出溝槽9，該切削屑排出溝槽9的溝 槽長度設定爲5.5mm以下。 此外’鑽孔工具之製造方法所製造的鑽孔工具，是由 具有刃部1之本體部2和柄部3所構成，前述刃部1是由 -8- 201024008 主成分爲碳化鎢及鈷之超硬合金構件4所形成，前述柄部 3是由不鏽鋼構件5所形成，將兩者熔接接合而構成鑽孔 工具；該製造方法的特徵在於：將前述超硬合金構件4和 前述不鏽鋼構件5藉由電阻熔接進行接合，以在前述超硬 合金構件4與前述不鏽鋼構件5的接合界面7之至少20% 以上的面積，使前述不鏽鋼構件5的鐵成分侵入前述超硬 合金構件4。 ❹ 此外’鑽孔工具之製造方法所製造的鑽孔工具，是由 具有刃部1之本體部2和柄部3所構成，前述刃部1是由 主成分爲碳化鎢及鈷之超硬合金構件4所形成，前述柄部 3是由不鏽鋼構件5所形成，將兩者熔接接合而構成鑽孔 工具；該製造方法的特徵在於：將前述超硬合金構件4和 前述不鏽鋼構件5藉由電阻熔接進行接合，以在前述超硬 合金構件4與前述不鏽鋼構件5的接合界面7之至少20% 以上的面積’使前述不鏽鋼構件5的鐵成分侵入前述超硬 Ο 合金構件4且朝該超硬合金構件4的侵入深度爲 5 - 0〜5 0.0 μιη 〇 此外’鑽孔工具之製造方法所製造的鑽孔工具，是由 具有刃部1之本體部2和柄部3所構成，前述刃部1是由 主成分爲碳化鎢及鈷之超硬合金構件4所形成，前述柄部 3是由不鏽鋼構件5所形成，將兩者熔接接合而構成鑽孔 工具；該製造方法的特徵在於：將前述超硬合金構件4和 前述不鏽鋼構件5藉由電阻熔接進行接合，以在前述超硬 合金構件4與前述不鏽鋼構件5的接合界面7之至少20% -9- 201024008 以上的面積，使前述超硬合金構件4的鈷成分脫落。 此外，鑽孔工具之製造方法所製造的鑽孔工具，是由 具有刃部1之本體部2和柄部3所構成，前述刃部1是由 主成分爲碳化鎢及鈷之超硬合金構件4所形成，前述柄部 3是由不鏽鋼構件5所形成，將兩者熔接接合而構成鑽孔 工具；該製造方法的特徵在於：將前述超硬合金構件4和 前述不鏽鋼構件5藉由電阻熔接進行接合，以在前述超硬 合金構件4與前述不鏽鋼構件5的接合界面7之至少2 0% 以上的面積，使前述超硬合金構件4的鈷成分脫落且從前 述接合界面7起算的脫落深度爲5.0~50.0μιη。 本發明由於採用上述的構造而能提供一種非常實用的 鑽孔工具及其製造方法，其不須使用焊料和化學藥品並能 減少超硬合金的使用量，可發揮充分的接合強度、能低成 本地製造且接合強度優異。The gist of the present invention will be described with reference to the accompanying drawings. The Q drilling tool is composed of a body portion 2 having a blade portion 1 and a shank portion 3, and the blade portion 1 is formed of a cemented carbide member 4 having a main component of tungsten carbide and cobalt, and the shank portion 3 is formed by The stainless steel member 5 is formed by welding the two together; the drilling tool is characterized in that the stainless steel member is made of an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 The iron component of 5 intrudes into the aforementioned superhard alloy member 4. Further, the drilling tool is composed of a main body portion 2 having a blade portion 1 and a shank portion -6-201024008 3, and the blade portion 1 is formed of a tungsten carbide and a superhard alloy member 4 having a main component, the aforementioned The shank portion 3 is formed by the stainless steel member 5 formed by welding the two together; the drilling tool is characterized by an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 The iron component of the stainless steel member 5 is invaded into the above-mentioned superhard alloy member 4; the penetration depth of the iron component toward the superhard alloy 4 is set to 5·0 to 50·0 μm. Further, the drilling tool is composed of a main body portion 2 having a blade portion 1 and a shank portion 3, and the blade portion 1 is formed of a tungsten carbide and a superhard alloy member 4 whose main component is tungsten carbide, and the shank portion 3 is formed. The stainless steel member 5 is formed by welding the two together; the drilling tool is characterized in that an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 is such that The cobalt component of the aforementioned superhard alloy member 4 falls off. Further, the drilling tool is composed of a main body portion 2 having a blade portion 1 and a shank portion 3, and the blade portion 1 is formed of a superhard alloy Φ gold member 4 whose main component is tungsten carbide and cobalt, and the shank portion 3 is formed of a stainless steel member 5 and welded together; the drilling tool is characterized in that an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 is The cobalt component of the cemented carbide member 4 is peeled off, and the peeling depth of the cobalt component is set to 5.0 to 50 μm from the joint surface 7 . Further, in the drilling tool according to claim 1, the superhard alloy member 4 and the stainless steel member 5 are joined by resistance welding. Further, in the drilling tool according to claim 2, the superhard alloy 201024008 member 4 and the stainless steel member 5 are joined by resistance welding. Further, in the drilling tool according to claim 3, the superhard alloy member 4 and the stainless steel member 5 are joined by resistance welding. Further, in the drilling tool of claim 4, the cemented carbide member 4 and the stainless steel member 5 are joined by resistance welding. In the drilling tool according to any one of claims 1 to 8, the joint portion 6 of the superhard alloy member 4 and the stainless steel member 5 including the joint interface 7 is provided in the main body portion 2 and The boundary of the shank portion 3 φ is closer to the position on the side of the main body portion 2 . In the drilling tool according to the ninth aspect of the invention, the joint portion 6 is provided in a range from the boundary between the main body portion 2 and the shank portion 3 to the front end of the main body portion 2 by 5 mm or less. Further, in the drilling tool according to claim 10, the length of the main body portion 2 is set to 5.0 to 7.0 mm. Further, in the drilling tool according to the eleventh aspect, the diameter of the base end portion of the super-hard alloy member 4 which is in contact with the stainless steel member 5 is set to _ 0.6 to 1 mm. Further, in the drilling tool according to claim 12, the diameter of the blade portion 1 is set to 〇.4 mm or less. Further, in the drilling tool according to the claim 13, the chip discharge groove 9 is formed on the outer periphery of the blade portion 1, and the groove length of the chip discharge groove 9 is set to 5.5 mm or less. In addition, the drilling tool manufactured by the manufacturing method of the drilling tool is composed of the main body portion 2 having the blade portion 1 and the shank portion 3, and the blade portion 1 is composed of -8-201024008, which is composed of tungsten carbide and cobalt. The superhard alloy member 4 is formed, and the shank portion 3 is formed of a stainless steel member 5, and the two are welded together to form a drilling tool; the manufacturing method is characterized in that the above-mentioned superhard alloy member 4 and the aforementioned stainless steel member 5 are Bonding by electric resistance welding causes the iron component of the stainless steel member 5 to intrude into the superhard alloy member 4 at an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5. Further, the drilling tool manufactured by the manufacturing method of the drilling tool is composed of the main body portion 2 having the blade portion 1 and the shank portion 3, and the blade portion 1 is a superhard alloy having a main component of tungsten carbide and cobalt. The member 4 is formed by the stainless steel member 5, and the two are welded together to form a drilling tool. The manufacturing method is characterized in that the superhard alloy member 4 and the stainless steel member 5 are made of a resistor. The welding is performed by joining, and the iron component of the stainless steel member 5 is invaded into the superhard niobium alloy member 4 at an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5, and is superhard. The intrusion depth of the alloy member 4 is 5 - 0 to 5 0.0 μm. Further, the drilling tool manufactured by the method of manufacturing the drilling tool is composed of the main body portion 2 having the blade portion 1 and the shank portion 3, and the aforementioned blade portion 1 is formed of a cemented carbide member 4 having a main component of tungsten carbide and cobalt, and the shank portion 3 is formed of a stainless steel member 5, and the two are welded together to form a drilling tool; the manufacturing method is characterized in that: The foregoing The superhard alloy member 4 and the stainless steel member 5 are joined by resistance welding so that the superhard surface is at least 20% -9 - 201024008 or more of the joint interface 7 of the aforementioned superhard alloy member 4 and the stainless steel member 5 The cobalt component of the alloy member 4 falls off. Further, the drilling tool manufactured by the method of manufacturing the drilling tool is composed of the body portion 2 having the blade portion 1 and the shank portion 3, and the blade portion 1 is a superhard alloy member having a main component of tungsten carbide and cobalt. 4, the handle portion 3 is formed of a stainless steel member 5, and the two are welded together to form a drilling tool; the manufacturing method is characterized in that the superhard alloy member 4 and the stainless steel member 5 are welded by resistance Bonding is performed so that the cobalt component of the cemented carbide member 4 is detached from the bonding interface 7 at an area of at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 It is 5.0~50.0μιη. The present invention can provide a very practical drilling tool and a manufacturing method thereof by adopting the above-described configuration, which can reduce the amount of use of the superhard alloy without using solder and chemicals, and can exhibit sufficient joint strength and low cost. It is manufactured and has excellent joint strength.
【實施方式】 G 簡單地說明本發明的較佳實施形態並根據圖式來顯示 本發明的作用。 藉由使超硬合金構件4和不鏽鋼構件5進行熔接接合 ，不須使用焊料和化學藥品並能減少超硬合金的使用量， 因此可低成本地製造，而且在超硬合金構件4與不鏽鋼構 件5的接合界面7以既定範圍讓不鏽鋼構件5的鐵成分侵 入超硬合金構件4，因此能將兩者非常強固地接合，而能 穩定地進行利用刃部1之鑽孔加工。 -10- 201024008 〔實施例〕 根據圖式來說明本發明的具體實施例。 本實施例的鑽孔工具，如第1圖所示，是由具有刃部 1之本體部2和柄部3所構成，前述刃部1是由主成分爲 碳化鎢及鈷之超硬合金構件4所形成，前述柄部3是由不 鏽鋼構件5所形成，將兩者熔接接合而構成鑽孔工具；在 φ 前述超硬合金構件4與前述不鏽鋼構件5的接合界面7之 至少20%以上的面積，使前述超硬合金構件4的鈷成分脫 落，該鈷成分從前述接合界面7起算的脫落深度設定爲 5.0〜50.Ομιη，且使前述不鏽鋼構件5的鐵成分侵入前述超 硬合金構件4，該鐵成分朝前述超硬合金構件4的侵入深 度設定爲5.0-50.Ομιη。 具體而言，是適用於印刷配線板的鑽孔加工之鑽頭， 其刃部的直徑Α (最大外徑）爲0.4mm以下，本體部的長 φ 度B爲5.0〜7.0mm，前述超硬合金構件4之與前述不鏽鋼 構件5接觸的基端部的直徑C爲0.6〜1.4mm。在刃部1的 外周，從前端朝向基端側形成螺旋狀的切削屑排出溝槽9 ，該切削屑排出溝槽9的溝槽長度D設定爲5.5 mm以下 。在本實施例，刃部直徑A約0.2 mm，本體部長度B約 6.0mm，超硬合金構件4的基端部的直徑C約l.Ornm，切 削屑排出溝槽9的溝槽長度D約5.0mm。 接著具體地說明各部分》 超硬合金構件4，如第3圖所示’是以碳化鎢和鈷（ -11 - 201024008 結合材）爲主成分之超硬合金製，其直徑比不鏽鋼構件5 (用來形成柄部3)小，是直徑大致相同的圓柱狀的棒材 〇 不鏽鋼構件5，是由麻田散鐵系不鏽鋼（主成分爲鐵 及鈷，含有微量的碳、矽、錳、磷及硫），是在與超硬合 金構件4的基端接合的前端側具有錐部8(往前端側漸細 )之圓柱狀棒材。以該錐部8的前端爲邊界可分成本體部 2和柄部3。在錐部8的前端，如第2圖所示設有：與超 @ 硬合金構件4的基端部的直徑大致相同且從錐部8的前端 稍微突出之對接部10。 將超硬合金構件4和不鏽鋼構件5藉由下述的電阻熔 接進行接合後，在超硬合金構件4的前端部形成刃部1而 構成第1圖所示的鑽孔工具。 超硬合金構件4和不鏽鋼構件5是藉由所謂電阻熔接 進行接合。該電阻熔接的過程，是讓超硬合金構件4的基 端部和不鏽鋼構件5的前端部（對接部10)對接，在對接 © 部分並未設置焊料等的第3材料，而在一定壓力下使兩者 壓接接觸的狀態下讓電流流過，利用物質間的接觸電阻發 熱使接觸部熔融而使成分彼此進行金屬熔合，藉此進行熔 接。 在本實施例，是在本體部2的基端部讓超硬合金構件 4和不鏽鋼構件5接合，以使接合界面7侵入本體部2側 〇 具體而言，在讓超硬合金構件4(超硬合金製的棒材 -12- 201024008 )的基端部和不鏽鋼構件5(不鏽鋼製的棒材）互相對接 並進行電阻熔接後，將超硬合金構件4的基端部及不鏽鋼 構件5的前端部實施除去加工（在本實施例爲磨削加工） 而做成第2圖或第3圖所示的形狀。亦即，使超硬合金構 件4的基端部形成圓柱狀’並在不鏽鋼構件5的前端部形 成錐部8和對接部10，然後不是以本體部2和柄部3的界 面（不鏽鋼構件5的錐部8的前端面）作爲接合界面（兩 φ 構件的對接面），而是加工成讓接合界面7形成在本體部 2側，將包含接合界面7之超硬合金構件4與不鏽鋼構件 5的接合部6設置在比本體部2與柄部3的邊界更接近本 體部2側的位置。 在本實施例，接合部6是設置在：從本體部2與柄部 3的邊界起算朝向本體部2的前端5.0mm以下的範圍內。 接合部6是指：位於超硬合金構件4的基端部和不鏽鋼構 件5的前端部且在接合界面7的附近，經由通電會發生熔 φ 融的部分。在本實施例，接合部6的形成寬度E是至少位 在本體部2側。此外，接合部6較佳爲設置在：從本體部 2與柄部3的邊界起算朝向本體部2的前端1.0mm以下的 範圍內。 因此，例如要在不鏽鋼構件5的錐部8(柄錐部）的 中途部（中間部）進行接合的情況，必須使超硬合金構件 4的基端側配合不鏽鋼構件5而變得大徑化，但藉由在本 體部2側形成接合界面7,就不須將基端側大徑化，而能 減少超硬合金的使用量。 -13- 201024008 因此，相較於習知品，能將本體部2的長度縮短 1.0mm以上，將超硬合金構件4的基端部的直徑縮小 0.2mm以上，且能避免在進行鑽孔加工時鑽孔工具前端所 受到的外力的影響。此外’超硬合金和不鏽鋼，由於物質 的縱彈性模數不同，不鏽鋼的彎曲量較大，或許被認爲在 本體部2的根部（基端部分）會發生應變變大的問題，但 實際上應力是集中在刃部1的根部，本體部2的根部之應 變並不會影響鑽孔時的性能這點已被確認。 @ 然而，在藉由電阻熔接進行接合的接合界面7，超硬 合金和不鏽鋼的成分彼此熔合，藉由界定該成分並求出最 佳量，即可實現接合強度穩定的接合。如第3圖所示將超 硬合金和不鏽鋼接合而製作出鑽孔工具的空白試樣（本體 部的長度B約6.0mm，柄部的長度約32.0mm，超硬合金 構件4的基端部的直徑（接合界面的直徑）C約1.0mm) ，對於超硬合金的前端部分，從橫向施加負載而使其破裂 ，利用應變計式測力計來測定負載並算出破裂應力，其結 果如第4圖所示。第4圖的縱軸代表破裂應力，橫軸代表 :從超硬合金與不鏽鋼的接合界面起算之超硬合金部中的 鈷成分的脫落深度。該脫落深度是依據以下方式來求出。 將超硬合金和不鏽鋼接合後沿長邊方向剖成兩半，將其表 面施以鏡面硏磨，對於該超硬合金和不鏽鋼的接合部，使 用X射線微分析儀（ΕΡΜΑ)，以加速電壓15kV、光束徑 Ομιη的條件將接合界面附近實施影像（mapping)分析（ 針對鎢成分和鈷成分），根據測定結果所檢測出的各成分 -14- 201024008 的濃度的最大値’與50%以上的鎢成分和鈷成分做比較而 求出。第6圖是以同樣的方式求出破裂應力和鐵成分的侵 入深度的結果。 從第4圖可確認出，從超硬合金與不鏽鋼的接合界面 起算，在超硬合金部的姑成分脫落深度在10.0~30·0μιη間 的破裂應力最大，在比該範圍更深或更淺的情況，破裂應 力降低。因此，爲了穩定地製造出可發揮穩定的性能之鑽 φ 孔工具，鈷成分的脫落深度宜在5.0〜50.0 μιη內。又從第6 圖可確認出，在鐵成分的侵入深度爲10.0〜3 0.0μιη之間破 裂應力最大。 第5圖係顯示：從超硬合金與不鏽鋼的界面起算，在 超硬合金部的鈷成分脫落深度的一例之ΕΡΜΑ影像。從第 5圖可確認出，在從超硬合金與不鏽鋼的界面起算 20.0〜30.0 μιη內的範圍鈷成分會脫落。在該脫落的部分， 有不鏽鋼成分之鐵成分（鉻成分）侵入。 φ 其理由在於：在電阻熔接的情況，在超硬合金和不鏽 鋼進行接合時，會在接合界面瞬間發生高溫，由於碳化鎢 成分比鈷成分、鐵成分、鉻成分的熔點更高，碳化鎢成分 不會熔融，但鈷成分、鐵成分、鉻成分會發生熔融，而分 別侵入不鏽鋼及超硬合金部。 因此，與鈷成分的脫落深度同樣的，鐵成分的侵入深 度也是宜在5.0~50.0μιη內。 此外，在ΕΡΜΑ影像分析中，爲了知道碳化鎢成分的 分布狀態而調查鎢成分的分布狀態。如此可界定出：在接 -15- 201024008 合界面，從超硬合金脫落的鈷成分之深度及寬度；從第5 圖可確認出，鈷成分之脫落寬度爲192μιη。在電阻熔接時 是瞬間從接合面的中心朝外周方向進行均等的接合，因此 鈷成分的脫落區域，是位在從接合面的中心朝向外周方向 的圓周上。從第5圖可確認出，鈷成分的脫落寬度，是呈 環狀存在於從接合面的中心起算168~360μιη之間（寬度 192μηι)，其面積占接合面積約41%。另外經由實驗而確 認出：鈷成分脫落且不鏽鋼成分（鐵成分）侵入的面積， q 若低於接合面積20%則破裂應力會明顯降低。因此，鈷成 分脫落且不鏽鋼成分（鐵成分）侵入的面積宜爲20%以上 〇 本實施例藉由採用以上的構造，藉由使超硬合金構件 和不鏽鋼構件進行熔接接合，不須使用焊料和化學藥品並 能減少超硬合金的使用量，因此可低成本地製造，而且在 超硬合金構件與不鏽鋼構件的接合界面以既定範圍讓不鏽 鋼構件的鐵成分以既定量侵入超硬合金構件，因此能將兩 @ 者非常強固地接合，而能穩定地進行鑽孔加工。 因此，本實施例不須使用焊料和化學藥品並能減少超 硬合金的使用量，可發揮充分的接合強度、能低成本地製 造且接合強度優異，是相當實用的。 【圖式簡單說明】 第1圖係本實施例的槪略說明側視圖。 第2圖係本實施例的主要部分之放大槪略說明側視圖 -16- 201024008 第3圖係超硬合金構件和不鏽鋼構件接合而形成刀部 之前的槪略說明側視圖。 第4圖係顯示從超硬合金構件的接合界面起算之鈷成 分的脫落深度和破裂應力的關係。 第5圖係顯示從超硬合金構件的接合界面之鈷成分的 脫落情況之ΕΡΜΑ影像。 φ 第6圖係顯示從超硬合金構件的接合界面起算之鐵成 分的侵入深度和破裂應力的關係。 【主要元件符號說明】 1 :刃部 2 :本體部 3 :柄部 4 :超硬合金構件 φ 5 :不鏽鋼構件 6 :接合部 7 :接合界面 9 :切削屑排出溝槽[Embodiment] G The preferred embodiment of the present invention will be briefly described and the operation of the present invention will be described based on the drawings. By fusion-bonding the cemented carbide member 4 and the stainless steel member 5, solder and chemicals are not required and the amount of use of the super-hard alloy can be reduced, so that it can be manufactured at low cost, and in the super-hard alloy member 4 and the stainless steel member. Since the joint interface 7 of the fifth member allows the iron component of the stainless steel member 5 to intrude into the cemented carbide member 4 within a predetermined range, the two can be joined very strongly, and the drilling process using the blade portion 1 can be stably performed. -10-201024008 [Embodiment] A specific embodiment of the present invention will be described based on the drawings. As shown in Fig. 1, the drilling tool of the present embodiment is composed of a main body portion 2 having a blade portion 1 and a shank portion 3, and the blade portion 1 is a superhard alloy member having a main component of tungsten carbide and cobalt. Formed at 4, the handle portion 3 is formed of a stainless steel member 5, and the two are welded together to form a drilling tool; at least 20% or more of the joint interface 7 between the cemented carbide member 4 and the stainless steel member 5 is φ. The area is such that the cobalt component of the cemented carbide member 4 is detached, and the peeling depth of the cobalt component from the joint interface 7 is set to 5.0 to 50. Ομηη, and the iron component of the stainless steel member 5 is invaded into the superhard alloy member 4 The penetration depth of the iron component toward the aforementioned superhard alloy member 4 is set to 5.0 to 50. Ομιη. Specifically, it is a drill which is suitable for drilling a printed wiring board, and has a diameter Α (maximum outer diameter) of the blade portion of 0.4 mm or less, and a length φ B of the main body portion of 5.0 to 7.0 mm, and the aforementioned superhard alloy The diameter C of the base end portion of the member 4 in contact with the aforementioned stainless steel member 5 is 0.6 to 1.4 mm. On the outer circumference of the blade portion 1, a spiral chip discharge groove 9 is formed from the tip end toward the base end side, and the groove length D of the chip discharge groove 9 is set to 5.5 mm or less. In the present embodiment, the blade portion diameter A is about 0.2 mm, the body portion length B is about 6.0 mm, the diameter C of the base end portion of the cemented carbide member 4 is about 1. Ornm, and the groove length D of the chip discharge groove 9 is about 5.0mm. Next, each part of the superhard alloy member 4 will be specifically described as shown in Fig. 3, which is made of a superhard alloy mainly composed of tungsten carbide and cobalt (-11 - 201024008), and has a diameter larger than that of the stainless steel member 5 ( The cylindrical rod-shaped stainless steel member 5 used to form the shank portion 3) is substantially the same diameter, and is made of granulated stainless steel (the main component is iron and cobalt, containing trace amounts of carbon, lanthanum, manganese, phosphorus and Sulfur is a cylindrical rod having a tapered portion 8 (narrowed toward the front end side) on the distal end side joined to the proximal end of the cemented carbide member 4. The body portion 2 and the shank portion 3 can be divided by the front end of the tapered portion 8. As shown in Fig. 2, the tip end portion of the tapered portion 8 is provided with an abutting portion 10 which is substantially the same as the diameter of the base end portion of the super @ hard alloy member 4 and slightly protrudes from the front end of the tapered portion 8. After the cemented carbide member 4 and the stainless steel member 5 are joined by the following resistance welding, the blade portion 1 is formed at the tip end portion of the cemented carbide member 4 to constitute the drilling tool shown in Fig. 1. The cemented carbide member 4 and the stainless steel member 5 are joined by so-called resistance welding. The process of welding the resistor is such that the base end portion of the cemented carbide member 4 and the front end portion (the butt portion 10) of the stainless steel member 5 are butted, and the third material such as solder is not provided in the butt portion, and under a certain pressure In a state in which the two are in contact with each other, a current flows, and the contact portion is heated by the contact resistance between the substances to melt the components, and the components are metal-fused to each other to be welded. In the present embodiment, the superhard alloy member 4 and the stainless steel member 5 are joined at the base end portion of the body portion 2 so that the joint interface 7 intrudes into the side of the body portion 2, specifically, the superhard alloy member 4 is super After the base end portion of the hard alloy bar -12-201024008 and the stainless steel member 5 (a bar made of stainless steel) are butted against each other and resistance-welded, the base end portion of the cemented carbide member 4 and the front end of the stainless steel member 5 are joined. The part is subjected to a removal process (grinding in this embodiment) to form a shape as shown in Fig. 2 or Fig. 3. That is, the base end portion of the cemented carbide member 4 is formed into a cylindrical shape 'and the tapered portion 8 and the abutting portion 10 are formed at the front end portion of the stainless steel member 5, and then the interface between the body portion 2 and the shank portion 3 is not used (the stainless steel member 5) The front end surface of the tapered portion 8 serves as a joint interface (the abutting surface of the two φ members), but is processed so that the joint interface 7 is formed on the body portion 2 side, and the cemented carbide member 4 and the stainless steel member 5 including the joint interface 7 are processed. The joint portion 6 is provided at a position closer to the body portion 2 than the boundary between the body portion 2 and the shank portion 3. In the present embodiment, the joint portion 6 is provided in a range of 5.0 mm or less from the boundary between the main body portion 2 and the shank portion 3 toward the front end of the main body portion 2. The joint portion 6 is a portion which is located at the base end portion of the cemented carbide member 4 and the front end portion of the stainless steel member 5 and which is melted by energization in the vicinity of the joint interface 7. In the present embodiment, the formation width E of the joint portion 6 is at least on the side of the body portion 2. Further, the joint portion 6 is preferably provided in a range of 1.0 mm or less from the boundary between the main body portion 2 and the shank portion 3 toward the front end of the main body portion 2. Therefore, for example, in the case where the intermediate portion (intermediate portion) of the tapered portion 8 (handle taper portion) of the stainless steel member 5 is joined, the proximal end side of the cemented carbide member 4 must be fitted with the stainless steel member 5 to be increased in diameter. However, by forming the joint interface 7 on the side of the main body portion 2, it is not necessary to increase the diameter of the base end side, and the amount of use of the superhard alloy can be reduced. -13- 201024008 Therefore, compared with the conventional product, the length of the main body portion 2 can be shortened by 1.0 mm or more, and the diameter of the base end portion of the cemented carbide member 4 can be reduced by 0.2 mm or more, and drilling during drilling can be avoided. The external force received by the front end of the hole tool. In addition, 'superhard alloy and stainless steel, due to the difference in the longitudinal elastic modulus of the material, the amount of bending of the stainless steel is large, and it may be considered that the strain at the root portion (base end portion) of the body portion 2 becomes large, but actually The stress is concentrated on the root of the blade portion 1, and the strain at the root portion of the body portion 2 does not affect the performance at the time of drilling. @ However, in the joint interface 7 joined by resistance welding, the components of the superhard alloy and the stainless steel are fused to each other, and by defining the component and obtaining the optimum amount, the joint with stable joint strength can be realized. A blank sample of the drilling tool was prepared by joining the cemented carbide and the stainless steel as shown in Fig. 3 (the length B of the body portion was about 6.0 mm, the length of the shank portion was about 32.0 mm, and the base end portion of the cemented carbide member 4). The diameter (diameter of the joint interface) C is about 1.0 mm. For the tip end portion of the cemented carbide, the load is applied from the lateral direction to break it, and the load is measured by a strain gauge type dynamometer, and the fracture stress is calculated. Figure 4 shows. The vertical axis of Fig. 4 represents the fracture stress, and the horizontal axis represents the peeling depth of the cobalt component in the superhard alloy portion from the joint interface of the cemented carbide and the stainless steel. This shedding depth is obtained in the following manner. After joining the super-hard alloy and the stainless steel, the two sides are cut in half along the long side, and the surface is mirror-honed. For the joint of the super-hard alloy and the stainless steel, an X-ray microanalyzer (ΕΡΜΑ) is used to accelerate the voltage. The condition of 15kV and the beam diameter Ομιη is performed by performing a mapping analysis (for the tungsten component and the cobalt component) in the vicinity of the joint interface, and the maximum 値' and 50% or more of the concentrations of the respective components -14 to 201024008 detected according to the measurement results. The tungsten component and the cobalt component were compared and found. Fig. 6 shows the results of the fracture stress and the penetration depth of the iron component in the same manner. It can be confirmed from Fig. 4 that, from the joint interface between the super-hard alloy and the stainless steel, the fracture stress in the super-hard alloy portion is between 10.0 and 30·0 μm, and is deeper or shallower than the range. In the case, the rupture stress is lowered. Therefore, in order to stably manufacture a drill hole tool which can exhibit stable performance, the peeling depth of the cobalt component is preferably within a range of 5.0 to 50.0 μm. Further, it can be confirmed from Fig. 6 that the fracture stress is the largest between the penetration depth of the iron component of 10.0 to 3 0.0 μm. Fig. 5 is a view showing an example of the depth of the cobalt component in the superhard alloy portion from the interface between the cemented carbide and the stainless steel. It can be confirmed from Fig. 5 that the cobalt component in the range of 20.0 to 30.0 μm is dropped from the interface between the cemented carbide and the stainless steel. In the detached portion, an iron component (chromium component) having a stainless steel component is invaded. The reason for φ is that in the case of resistance welding, when the cemented carbide and the stainless steel are joined, a high temperature is instantaneously generated at the joint interface, and since the tungsten carbide component has a higher melting point than the cobalt component, the iron component, and the chromium component, the tungsten carbide component It does not melt, but the cobalt component, the iron component, and the chromium component melt, and invade the stainless steel and the super-hard alloy portion, respectively. Therefore, the penetration depth of the iron component is preferably within the range of 5.0 to 50.0 μm as the depth of the cobalt component. Further, in the ΕΡΜΑ image analysis, the distribution state of the tungsten component was investigated in order to know the distribution state of the tungsten carbide component. Thus, the depth and width of the cobalt component peeled off from the superhard alloy at the interface of -15-201024008 can be defined. From Fig. 5, it can be confirmed that the peeling width of the cobalt component is 192 μm. When the resistance is welded, the joint is uniformly joined from the center of the joint surface to the outer circumferential direction. Therefore, the drop region of the cobalt component is located on the circumference from the center of the joint surface toward the outer circumferential direction. From Fig. 5, it was confirmed that the peeling width of the cobalt component was in the form of a ring from 168 to 360 μm (width: 192 μm) from the center of the joint surface, and the area thereof was about 41%. Further, it was confirmed by experiments that the area where the cobalt component fell off and the stainless steel component (iron component) invaded, and q was less than 20% of the joint area, the fracture stress was remarkably lowered. Therefore, the area where the cobalt component falls off and the stainless steel component (iron component) intrudes is preferably 20% or more. In the present embodiment, by using the above structure, the superhard alloy member and the stainless steel member are welded and joined without using solder and Since the chemical can reduce the amount of use of the superhard alloy, it can be manufactured at low cost, and the iron component of the stainless steel member is intruded into the superhard alloy member in a predetermined range at the joint interface between the cemented carbide member and the stainless steel member. The two @ can be joined very strongly, and the drilling process can be performed stably. Therefore, this embodiment is not practical in that it can reduce the amount of use of the superhard alloy without using solder and chemicals, and can exhibit sufficient joint strength, can be manufactured at low cost, and has excellent joint strength. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a schematic side view showing the present embodiment. Fig. 2 is a side elevational view of a main portion of the present embodiment. -16 - 201024008 Fig. 3 is a schematic side view showing a state in which a superhard alloy member and a stainless steel member are joined to form a blade portion. Fig. 4 is a graph showing the relationship between the peeling depth of the cobalt component and the fracture stress from the joint interface of the cemented carbide member. Fig. 5 is a view showing the detachment of the cobalt component from the joint interface of the cemented carbide member. φ Fig. 6 shows the relationship between the penetration depth of the iron component and the fracture stress from the joint interface of the cemented carbide member. [Main component symbol description] 1 : Blade 2 : Main body 3 : Handle 4 : Superhard alloy member φ 5 : Stainless steel member 6 : Joint portion 7 : Joint interface 9 : Chip discharge groove