TW201250010A - Method for producing cold-work die - Google Patents
Method for producing cold-work die Download PDFInfo
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- TW201250010A TW201250010A TW101105391A TW101105391A TW201250010A TW 201250010 A TW201250010 A TW 201250010A TW 101105391 A TW101105391 A TW 101105391A TW 101105391 A TW101105391 A TW 101105391A TW 201250010 A TW201250010 A TW 201250010A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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Abstract
Description
201250010 六、發明說明: 【發明所屬之技術領域】 本發明係有關於將例如家電、行動電話及汽車相關 零件成形之冷作加工用模具之製造方法。 【先前技術】 在室溫之板材的彎曲、拉製、沖壓等的加壓成形所 使用之冷作加工用模具,為了提升其耐摩耗性,有提案 種藉由淬火回火(以下稱為「調質」)而能夠達成55时。 以上的硬度之鋼链料(專利文獻丨至3) ^若形成為此種高 硬度的鋼述料,則在調質後要切削加工成為模具形狀係 為困難。ϋ此’通常係在將鋼塊熱作加工後之硬度較低 的退火狀態進行粗加工之後,調質成為55HRC以上的使 用硬度。此時’由於調質弓丨起模具發生熱處理變形,所 以調質後;^加再次之最後完成切削加工以修正其變形 分之而調整成為最終模具形狀。調質引起模具的熱處理 變形之主要原因,係由於在退火狀態時為肥粒鐵(ferrite) 組織之鋼:¾料變相成為麻田散鐵(_tensite)組織而體積 膨脹之故。 上述的鋼坯料以外,有許多提案預先調質至使用硬 度而供給之預硬鋼。預硬鋼由於在進行成批切削加工至 最後模具形狀之後’不必調質,能夠免除起因於調質之 模具的熱處理變形,亦能夠省略上述的最後切削加工之 有效的技術。關於本技術’有提案一種冷作工具鋼,其 係藉由將在淬火回火後的鋼坯料甲存在之使切削性降低 之未固奴化物的量最適化,而在確保大於的調 201250010 質硬度之同時,具有優良的切削性(專利文獻4)。另一方 面為了抑制切削加工時的切削工具與鋼炫料之間的摩 擦而產生之工具摩耗,亦有提案一種冷作工具鋼,其係 添加形成炫點為UOOt以下的氧化物(有(FeO)2、. Si〇2、201250010 VI. Description of the Invention: [Technical Field of the Invention] The present invention relates to a method of manufacturing a mold for cold working for molding, for example, home appliances, mobile phones, and automobile-related parts. [Prior Art] In the cold working die used for press forming, such as bending, drawing, and pressing of a sheet at room temperature, in order to improve the wear resistance, there is a proposal to quench and temper (hereinafter referred to as " It can be achieved at 55 o'clock. The steel chain of the above hardness (Patent Documents 丨 to 3) ^ If it is formed into such a high-hardness steel material, it is difficult to cut into a mold shape after quenching and tempering. ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ ’ At this time, the heat treatment deformation of the mold is caused by the quenching bow, so that after the quenching and tempering, the final machining is completed to correct the deformation and the final mold shape is adjusted. The main reason for the heat treatment deformation of the mold caused by the quenching and tempering is that the steel which is the ferrite structure in the annealed state has a volume expansion due to the phase change of the material into the _tensite structure. In addition to the above-mentioned steel billets, there are many proposals for pre-tempering to pre-hardened steel which is supplied with hardness. Since the pre-hardened steel is not required to be tempered after performing the batch cutting process to the final mold shape, the heat treatment deformation of the mold due to the quenching and tempering can be eliminated, and the above-described effective technique for the final cutting can be omitted. Regarding the present technology, there is proposed a cold-work tool steel which is optimized by ensuring that the amount of unsolidified material which reduces the machinability in the presence of the steel billet after quenching and tempering is ensured to be greater than the 201250010 quality. It has excellent machinability at the same time as hardness (Patent Document 4). On the other hand, in order to suppress the tool wear caused by the friction between the cutting tool and the steel material during the cutting process, there is also proposed a cold-work tool steel which is added to form an oxide having a bright point of less than UOOt (with (FeO) 2, Si〇2
Fe2Si04或(FeSi)Cr2〇2)之元素,藉此,利用切削力口工時 所產生熱量而在模具表面,形成前述氧化物以賦予自潤 滑性(專利文獻5 )。 [先前技術文獻] [專利文獻] L專利文獻1]特開20084 89982號公報 [專利文獻2]特開2009-1 32990號公報 [專利文獻3]特開2006-193790號公報 [專利文獻4]特開2001-316769號公報 [專利文獻5]特開2005-272899號公報 【發明内容】 [發明欲解決之課題] 、 最近’冷作加工用模具的使用條件之嚴苛度增加,By the element of Fe2Si04 or (FeSi)Cr2〇2), the oxide is formed on the surface of the mold by the heat generated by the cutting force to impart self-lubricity (Patent Document 5). [PATENT DOCUMENT] [Patent Document 1] JP-A-2008-193790 (Patent Document 3) JP-A-2006-193790 (Patent Document 4) [Patent Document 5] JP-A-2005-272899 [Summary of the Invention] [Problems to be Solved by the Invention] Recently, the severity of use conditions of molds for cold working has increased,
冷作工具鋼係被要求能夠達成58HRC以上、進而60HRCCold work tool steel system is required to achieve 58HRC or more, and then 60HRC
:上的淬火回火硬度8因此’預硬鋼的情形,上述58 HRC 乂上的硬度係為當$ ’較佳為能夠安定地得到以 上的硬度,而Η + 且在其鬲硬度狀態具有優異的切削性。在 專利文獻4所揭示的冷作工具鋼係兼具切削加工時的切 肖U生及作為模具之耐摩耗性之優異的預硬鋼。但是,針 對耐摩耗性,因為必 兩除了規疋未固溶ί炭化物的形成量少以 外,,泮火溫度亦祐 J被限制,所以若要成為60HRC以上的調 201250010 質硬度’能夠得到此之成分範圍非常地受到限定。而且 ’為了抑制淬火加熱時的結晶粒成長之目的,在 獻4認為較佳添加之N b和v,係在上述的泮火溫度容 未固溶的MC碳化物之元素。因為MC碳化物係為硬質, 在專利文獻4所揭示之成分組成,有調質後的切削性 低落之問題。 … 又在專利文獻5所揭示之冷作工具鋼,係將低炫點 氧化物利用作為自满滑皮膜,但是在切削溫度未上升至 氧化物的熔點之情況,則無法得到潤滑效果。相反地, 切肖! 度過度上升的情況,則氧化物的黏度顯著低落而 有無法達成作為潤滑皮膜的功能之問題。 本發明的目的係提供一種將冷作工具鋼以58〜62Hr 調質硬度切削加工之冷作加工用模具之製造方法,該冷 作工具鋼,58HRC以上的硬度係為當然,以可安定地達 成60HRC以上的高調質硬度之成分組成作為基本,較佳 為即便進一步增加未固溶碳化物的形成量,亦不依存於 切削溫度而飛躍性地提升調質後的切削性。 [解決課題之手段] 本發明者專心研究提升冷作工具鋼的切削性之手法 。其結果’發現藉由積極地導入兩溶點氧化物之A12 〇 3 ,利用切削加工時之熱而在切削工具的表面形成包含其 及高延展性夾雜物亦即MnS之複合潤滑保護皮膜之手法 。而58HRC以上係當然爾,亦達成60HRC以上的高調質 硬度’能夠形成該複合潤滑保護皮膜之鋼链料係有最適 合的成分範圍,藉由將其特定而達成了本發明。 201250010 亦即,本發明係一種冷作加工用模具之製造方法, 其特徵在於:對包含以質量%計為 C· 0.6〜1.2%、: The quenching and tempering hardness of the upper 8 is therefore the case of the pre-hardened steel. The hardness of the above-mentioned 58 HRC crucible is such that when it is preferable, the above hardness can be obtained stably, and Η + is excellent in the crucible hardness state. Machinability. The cold-work tool steel disclosed in Patent Document 4 has both a cut-off and a pre-hardened steel which are excellent in wear resistance of the mold. However, in terms of wear resistance, the amount of simmering is not limited, and the simmering temperature is also limited. Therefore, it is possible to obtain the hardness of 201250010 of 60HRC or higher. The range of ingredients is very limited. Further, in order to suppress the growth of crystal grains during quenching heating, it is considered that Nb and v which are preferably added are elements of the MC carbide which are not solid-solved at the above-mentioned anneal temperature. Since the MC carbide is hard, the composition of the components disclosed in Patent Document 4 has a problem that the machinability after quenching and tempering is low. Further, in the cold-work tool steel disclosed in Patent Document 5, the low-spot oxide is used as the compensatory slip film, but the lubrication effect cannot be obtained when the cutting temperature does not rise to the melting point of the oxide. On the contrary, cut off! When the degree is excessively increased, the viscosity of the oxide is remarkably lowered, and there is a problem that the function as a lubricating film cannot be achieved. The object of the present invention is to provide a method for manufacturing a cold working tool for cutting cold working tool steel with a quenching and tempering hardness of 58 to 62 Hr. The hardness of the cold working tool steel of 58 HRC or more is of course stable. Basically, the composition of the high-tempering hardness of 60 HRC or more is preferable, and even if the amount of formation of the undissolved carbide is further increased, the machinability after quenching and tempering is drastically improved without depending on the cutting temperature. [Means for Solving the Problem] The inventors focused on the technique of improving the machinability of cold-work tool steel. As a result, it was found that by actively introducing A12 〇3 of two melting point oxides, a method of forming a composite lubricating protective film containing MnS, which is a high ductility inclusion, or a high ductility inclusion, on the surface of the cutting tool by heat during cutting is used. . On the other hand, in the case of 58 HRC or more, the high-tempering hardness of 60 HRC or more is also achieved. The steel chain material capable of forming the composite lubricating protective film has the most suitable composition range, and the present invention has been achieved by specifying it. 201250010 That is, the present invention is a method for producing a mold for cold working, characterized in that it comprises C·0.6 to 1.2% by mass%,
Si : 0.8-2.5% ^ Μη : 0.4〜2.0%、 S : 0.03〜0.1%、Si : 0.8-2.5% ^ Μη : 0.4 to 2.0%, S: 0.03 to 0.1%,
Cr : 5.0〜9.0%、Cr : 5.0 to 9.0%,
Mo及W以單獨或複合為(MO+1/2W) : 0.5〜2.0%、 A1 : 〇.〇4〜小於 0.3%、 剩餘部分Fe及不可避免的不純物之冷作工具鋼的鋼塊, 進行熱作加工而作為坯料,並且將該坯料進行淬火回火 而將硬度調質成為58〜62HRC之後,進行切削加工而完成 加工成為模具的形狀。作為一具體例,係在進行熱作加 工後之场料’進行退火之後,進行淬火回火之冷作加工 用模具之製造方法。而且,作為另一具體例,淬火係在 前述熱作加工後的冷卻過程進行之直接淬火的冷作加工 用模具之製造方法。較佳是調質後的硬度為6〇hrC以上 〇 ^本發明之冷作工具鋼係亦可含有1 ·0%以下的Ni、或 是進一步含有1.0%以下的Cu。 而且,關於本發明之冷作 kO%以下的V、或是再進—步 [發明之效果] 作工具鋼,亦可進一步含有 步含有0.5%以下Nb。Mo and W are made of steel blocks of cold work tool steel, either alone or in combination (MO+1/2W): 0.5~2.0%, A1: 〇.〇4~ less than 0.3%, the remaining part of Fe and unavoidable impurities. After hot working, it is used as a billet, and the billet is quenched and tempered to adjust the hardness to 58 to 62 HRC, and then subjected to cutting processing to complete the processing into a shape of a mold. As a specific example, a method of manufacturing a mold for cold working by quenching and tempering after annealing the field material after the hot working is performed. Further, as another specific example, the quenching is a method of producing a mold for cold working which is directly quenched by the cooling process after the hot working. Preferably, the hardness after quenching and tempering is 6 〇 hr C or more. 〇 The cold working tool steel of the present invention may further contain 1.0% or less of Ni or further 1.0% or less of Cu. Further, the tool steel may be further contained in the step of containing 0.5% or less of Nb in the step of the cold work kO% or less of the cold work of the present invention.
因為採用能夠廣泛地對應多數的成分 的手段,58HRC以上係為當然,即便 201250010 調質成為60HRC以上的硬度,而且未固溶碳化物量多之 合金設計’亦能夠不依存於切削溫度而可作為調質後的 切削性飛躍性地提升之冷作工具鋼。因此,能㈣由地 選擇冷作工具鋼的調質硬度、或是按照各種功能之未固 溶碳化物*。而且,若將該冷作工具鋼調質成為 58〜62獄的硬度之後進行切削加卫,因為能夠解決有關 熱處理變形和再次的最後完成#工之課題而製造模且, 特別是對於利用預硬冷作工具鋼之冷作加工用模具的實 用化’係成為不可缺少之技術。 【實施方式】 [實施發明之形態] 本發明之特徵係在於:先將調質硬度提升之後,即 使在為了控制結晶粒徑等而形成大量未固溶碳化物之情 況,亦能夠實現調質後的切削性不依存於溫度之良好的 冷作工具鋼,而將該調質後的冷作工具鋼進行加工。具 體而言’係除了可得到58HRC以上、較佳6〇HRC以上的 調質硬度以外,為了抑削切削工具的摩耗,將鋼坯料經 成分s又汁之冷作工具鋼在切削加工之前調質,該冷作工 具鋼係使高熔點氧化物之A12〇3及高延展性夹雜物之 Μ n S的複合潤滑保護皮膜形成在切削工具的表面。 首先,本發明者檢討能夠廣泛地對應冷作工具鋼的 成分組成之提升切削性的手段。其結果,注目在自潤滑 性的有效性。而且在檢討如專利文獻5之利用低熔點氧化 物的自潤滑性的作用效果時,查明了其有依存於切削溫 度之課題。亦即,因為具有自潤滑性之低熔點氧化物, 達成了本發明 以下針對關於本發明的製造方法之 201250010 通节係為含有大量地被含有在鋼坯料中之Fe和Cr的 氧化物’因切削溫度的變動,複合氧化物的成分和 量會大幅度地變動’而無法得到安定的潤滑效果。 θ在此,本發明係專心研究不以利用低熔點氧化 提升冷作工具鋼的切削性之手法時,相反地發現 積極,I入高熔點氧化物之八丨2〇3,利用切削加工時 使其及高延展性夾雜物之MnS的複合潤滑保 膜在削工具的表面形成之手法◊此複合潤滑保護 係對應廣闊範圍的切削溫度而效果不會變動,而且 添加形成Nb和v之硬質的MC碳化物之元素時亦能 保良好的切削'性。而且58HRC以上的硬度係當然爾 達成60HRC以上的調質硬度,能夠形成該複合潤滑 皮膜之鋼坯料係有最適合的成分範圍,藉由將其特 工具鋼的成分組成進行說明。 .(:.0.6~1.2質量%(以下僅記載為%) C係在鋼中形成碳化物且對冷作工具鋼賦予硬 重要元素太上時’所形成之碳化物量係不足,使 5 8HRC以上、較佳為6〇HRC以上係為困難。另一方 過多的含有,會因為淬火時的未固溶碳化物量之增 使動性容易降低*。因此,使C的含量係為〇·6〜i 2%, 為〇·7%以上及/或M%以下,更佳為1.0%以下。 .Si : 0.8〜2.5%Because it is a means that can widely correspond to a large number of components, it is a matter of course that 58HRC or more, even if the 201250010 is tempered to a hardness of 60HRC or more, and the alloy design having a large amount of solid solution-free carbide can be adjusted without depending on the cutting temperature. The cold work tool steel is greatly improved by the machinability after the quality. Therefore, it is possible to (4) select the quenching hardness of the cold-work tool steel or the undissolved carbide* according to various functions. In addition, if the cold-work tool steel is tempered to a hardness of 58 to 62 prisons, it is cut and reinforced, because it can solve the heat treatment deformation and the final completion of the work, and the mold is produced, especially for the use of pre-hardening. The practical use of cold working tool steel for cold work tooling is an indispensable technology. [Embodiment] The present invention is characterized in that after the tempering hardness is first improved, even after a large amount of undissolved carbide is formed to control the crystal grain size or the like, the tempering can be achieved. The machinability is not dependent on the good cold work tool steel, and the tempered cold work tool steel is processed. Specifically, in addition to obtaining a quenched and tempered hardness of 58 HRC or more, preferably 6 HRC or more, in order to suppress the wear of the cutting tool, the steel billet is tempered by the component s and the cold of the tool steel before the cutting process. The cold working tool steel forms a composite lubricating protective film of a high melting point oxide A12〇3 and a high ductility inclusion Μn S on the surface of the cutting tool. First, the inventors reviewed means capable of broadly meeting the improved machinability of the composition of the cold-work tool steel. As a result, attention is paid to the effectiveness of self-lubricity. Further, when examining the effect of the self-lubricating property of the low-melting-point oxide as in Patent Document 5, it was found that it has a problem depending on the cutting temperature. That is, since the low melting point oxide having self-lubricity achieves the present invention, the following 201250010 section for the manufacturing method of the present invention is an oxide containing a large amount of Fe and Cr contained in the steel material. The variation in the cutting temperature causes the composition and amount of the composite oxide to vary greatly, and the stable lubricating effect cannot be obtained. θ Here, the present invention concentrates on the method of improving the machinability of cold-work tool steel by utilizing low melting point oxidation, and conversely finds that it is active, I enter the high melting point oxide of 丨2〇3, using cutting processing. The composite lubrication coating of MnS and the high-ductility inclusions is formed on the surface of the cutting tool. The composite lubrication protection system does not change the cutting temperature corresponding to a wide range, and the hard MC forming Nb and v is added. Good cutting properties are also achieved when the elements of carbide are used. Further, the hardness of 58 HRC or more is of course a quenched and tempered hardness of 60 HRC or more, and the steel billet which can form the composite lubricating film has the most suitable component range, and the composition of the special tool steel is described. (: 0.6 to 1.2% by mass (hereinafter only referred to as %) When the C system forms carbides in steel and imparts hard important elements to the cold-work tool steel, the amount of carbide formed is insufficient, making it more than 5 8HRC. Preferably, it is difficult to be 6 〇HRC or more. If the other side is excessively contained, the kinetic property is easily lowered due to an increase in the amount of undissolved carbide at the time of quenching. Therefore, the content of C is 〇·6~i 2%, 〇·7% or more and/or M% or less, more preferably 1.0% or less. .Si : 0.8 to 2.5%
Si係固/谷於鋼中,且係對冷作工具鋼職予硬度 要元素。又,除了氧化傾向比Fe或Cr強,因為係容 複合 形成 物而 藉由 之熱 護皮 皮膜 即便 夠確 ,亦 保護 定而 冷作 度之 賦予 面, 力口而 較佳 之重 易與 201250010 Α1ζ〇3形成剛玉(corundum)系的氧化物之元素,而在本發 明中抑制使氧化物低熔點化之Fe系氧化物和Cr系氧化物 的形成,而具有促進Ah〇3保護皮膜的形成之重要的作用 。但是,過多時淬火性和韌性則顯著地降低。因此,使 Si為0.8〜2.5/ί>,較佳為1.0%以上及/或2.0%以下,更佳為 1.2 %以上。 • Μη : 0.4〜2.0% Μη係本發明之重要元素,其係在切削工具表面所形 成之Al2〇3保護皮膜上作為良好的潤滑皮膜而作用。而且 係沃斯田體(austenite)形成元素,在鋼中固溶而提升淬火 性。但是’添加量過多時,則在調質後大量地殘留殘留 沃斯田體’而成為作為模具使用時之經年尺寸變化的原 因。又,因為容易與Fe* Cr形成低熔點氧化物,而成為 阻礙AhO3保護皮膜的功能之重要因素。因此,在本發明 係設為0 · 4〜2.0 % ’較佳為〇 6 %以上及/或1 5 %以下。 • S : 0.03〜0.1〇/〇 S係本發明之重要元素,其係在切削工具表面所形成 之AhO3保護皮膜上作為良好的潤滑皮膜而作用。亦即在 鋼料中所含有之充分量的S形成MnS。而且,MnS除了 富有延展性’因為與Al2〇3的親和性良好,在a1203保護 皮崩:上沉•積’而達成作為良好的複合潤滑保護皮膜之任 務。為了充分地發揮此種潤滑作用,必要添加0 03%以上 ’但是因為S會使鋼的韌性變差,設上限為0.1 %。較佳為 0 · 0 4 %以上及/或〇 〇 $ %以下。 .Cr : 5.0〜9.〇〇/0 -10- 201250010The Si solid/valley is in the steel and is a hardening element for the cold work tool steel. In addition, the oxidation tendency is stronger than that of Fe or Cr. Because the composite composite is formed by the thermal protective film, even if it is correct, it protects the surface of the cold work, and the pressure is better and the 20125010 Α1ζ 〇3 forms an element of a corundum-based oxide, and in the present invention, it inhibits the formation of a Fe-based oxide and a Cr-based oxide which lower the melting point of the oxide, and promotes the formation of the Ah〇3 protective film. Important role. However, when too much, the hardenability and toughness are remarkably lowered. Therefore, Si is made 0.8 to 2.5/ί>, preferably 1.0% or more and/or 2.0% or less, more preferably 1.2% or more. • Μη: 0.4 to 2.0% Μη is an important element of the present invention and functions as a good lubricating film on the Al2〇3 protective film formed on the surface of the cutting tool. Moreover, it forms elements in the austenite and solidifies in steel to improve hardenability. However, when the amount of addition is too large, a large amount of residual Worth field body remains after the quenching and tempering, and this causes a change in the dimensional change of the year when used as a mold. Further, since it is easy to form a low melting point oxide with Fe*Cr, it is an important factor that hinders the function of the AhO3 protective film. Therefore, in the present invention, it is preferably 0. 4 to 2.0%', preferably 〇 6 % or more and/or 15 % or less. • S: 0.03 to 0.1 〇/〇 S is an important element of the present invention and functions as a good lubricating film on the AhO3 protective film formed on the surface of the cutting tool. That is, a sufficient amount of S contained in the steel material forms MnS. Further, in addition to being ductile, MnS has a good affinity for Al2〇3, and protects the skinfold from a1203: sinking and accumulating to achieve a good composite lubrication protective film. In order to fully exert such a lubricating action, it is necessary to add 0 03% or more. However, since S deteriorates the toughness of the steel, the upper limit is made 0.1%. It is preferably 0 · 0 4 % or more and / or 〇 〇 $ % or less. .Cr : 5.0~9.〇〇/0 -10- 201250010
Cr係藉由在調質後的組螺中报士u p„仏 J、且螂甲形成ΜΑ3碳化物,而賦 予冷作工具鋼硬度。又,在海令‘拥。* 仗/平火加熱時一部分係作為未 固溶碳化物存在,而有抑制結晶粒的成長之效果。且藉 由將Cr設為5.0%以上,所形成之碳化物量變多,能夠充 分地達成58HRC以上、較佳為6〇HRC以上之硬度。再者 ,在作為冷作加工用模具時的表面,進行各種:覆處理 時,能夠提升藉由TD處理之vc皮膜與藉由cvd處理之The Cr system imparts hardness to the cold-work tool steel by means of the sergeant in the group of snails after quenching and tempering, and the 螂3 carbide is formed in the armor. In addition, in the case of the sea order, the 海/仗火加热In some cases, the amount of carbide formed is increased by 5.0% or more, and the amount of carbide formed is increased to a maximum of 58 HRC or more, preferably 6 or less.硬度HRC or higher hardness. In addition, when used as a mold for cold working, various types of coatings can be used to improve the vc film treated by TD and treated by cvd.
TiC皮膜的形成能力。又,在確保耐蝕性上,&係有效的 元素。 另一方面,冷作工具鋼的主要成分之&,係容易形 成低熔點氧化物。亦即過多地含有〇時,會成為阻礙 Ah〇3保護皮膜的功能之重要因素。該結果,會成為阻礙 作為本發明的特徵之包含A12 〇 3及μ n S之複合潤滑保護 皮膜的功能之重要因素。因此,在後述之含有充分量的 Α1之基礎上’調整Cr係重要的。而且,藉由進行與其相 稱之S量的調整,能夠發揮上述複合潤滑保護皮膜的功能 »因此,設Cr為5.0〜9.0〇/〇係重要的。較佳為6 〇%以上, 更佳為7.0%以上。 .Mo及W係以單獨或複合且(MO+1/2W) : 0.5〜2.0〇/〇The formation ability of the TiC film. Moreover, & is an effective element in ensuring corrosion resistance. On the other hand, the main component of the cold-work tool steel is easy to form a low-melting oxide. That is, when the sputum is excessively contained, it becomes an important factor that hinders the function of the Ah〇3 protective film. As a result, it is an important factor that hinders the function of the composite lubricating protective film containing A12 〇 3 and μ n S which is a feature of the present invention. Therefore, it is important to adjust the Cr system in addition to a sufficient amount of Α1 to be described later. Further, by performing the adjustment of the S amount which is commensurate with it, the function of the above-mentioned composite lubricating protective film can be exhibited. Therefore, it is important to set Cr to 5.0 to 9.0 Å/〇. It is preferably 6 〇% or more, more preferably 7.0% or more. .Mo and W are either alone or composite and (MO+1/2W): 0.5~2.0〇/〇
Mo及W係在調質時的回火,藉由強化析出(二次硬化 )微細碳化物而使硬度提升之元素。但是同時,因為會使 在回火產生之殘留沃斯田體的分解遲滯,過多地含有時 ’殘留沃斯田體係容易殘留在調質後的組織。又,因為 Mo和W係昂貴的元素’在實用化上應盡力減低添加量。 因此,設該等元素的添加量以(M〇+1/2w)的關係式為 -11- 201250010 0.5〜2.0% 0 • A1 : 〇·〇4〜小於 0.3% Α1係本發明之重要元素,亦即在鋼坯料中所含有之 充分里的Α1,係藉由切削加工時所產生的熱而在切削工 具表面形成高熔點氧化物之Μ"3 β Μ"3的熔點係約 2050t,因為其比切削溫度高出甚多’幻2〇3係作為切削 工具的保護皮膜而作用》而且,藉由含有〇〇4%以上,能 夠形成充分的厚度之保護皮膜而改善工具壽命。但是^ 量地添加A1時,因為在鋼坯料中’ Ah〇3係作為夾雜物大 量地形成,鋼坯料的切削性反而降低。因此,設ai的添 加ϊ之上限為小於〇·3%。較佳為〇.〇5%以上及/或〇 15%以 下。 •較佳是Ni : 1 ·〇%以下Mo and W are tempering at the time of quenching and tempering, and are elements which enhance hardness by strengthening precipitation (secondary hardening) of fine carbides. At the same time, however, the decomposition of the residual Worth field caused by tempering is delayed, and when it is excessively contained, the residual Vastland system tends to remain in the tempered structure. Further, since Mo and W are expensive elements, the amount of addition should be reduced as much as possible in practical use. Therefore, it is assumed that the relationship between the addition amount of these elements is (M〇+1/2w) is -11-201250010 0.5~2.0% 0 • A1 : 〇·〇4~ less than 0.3% Α1 is an important element of the present invention, That is, the Α1 contained in the steel billet is a high melting point oxide formed on the surface of the cutting tool by the heat generated during the cutting process, and the melting point of the "3 β Μ" 3 is about 2050 t because The cutting temperature is much higher than the cutting temperature. The phantom 2 〇 3 system acts as a protective film for the cutting tool. Further, by containing 〇〇 4% or more, it is possible to form a protective film having a sufficient thickness to improve the tool life. However, when A1 is added in a large amount, since the ' Ah 〇 3 system is formed as a large amount of inclusions in the steel material, the machinability of the steel slab is rather lowered. Therefore, the upper limit of the addition of ai is set to be less than 〇·3%. Preferably, it is 〇. 5% or more and/or 〇 15% or less. • preferably Ni: 1 ·〇% or less
Ni係改善鋼的韌性和焊接性之元素。又因為調質 時之回火係作為NhAl析出而具有提高鋼的硬度之效果 ’按照關於本發明之冷作工具鋼所含有的八丨量而添加係 為有效》但是,Ni係昂貴金屬’在實用化上應盡力減低 添加量。因此,本發明之Ni,在添加時亦以i 〇〇/〇以下為 較佳。 •較佳是Cu : 1 ·0%以下Ni is an element that improves the toughness and weldability of steel. Further, since the tempering at the time of conditioning is an effect of increasing the hardness of the steel as NhAl precipitation, it is effective to add the amount of the tantalum contained in the cold-work tool steel of the present invention. However, the Ni-based expensive metal is Practical efforts should be made to reduce the amount of addition. Therefore, Ni of the present invention is preferably i 〇〇 / 〇 or less at the time of addition. • preferably Cu: 1 · 0% or less
Cu係在調質時的回火時作為e_Cu析出而具有提高鋼 的硬度之效果。但是,Cu係造成鋼坯料的熱作脆性之元 紊。因此,本發明之Cu係添加時亦以丨〇%以下為較佳。 叉,因為由於Cu之熱作脆性能夠藉由添加大約同量的別 而抑制,關於本發明之冷作工具鋼在含有Ni時,能夠按 •12- 201250010 照該量而緩和限制值β •較佳是V : 1. 〇 %以下 V係形成各種的碳化物而具有提高鋼的硬度之效果 。又’所形成之未固溶的MC碳化物係具有抑制結晶粒成 長之效果。而且特別是藉由與後述的合添加,在淬 火加熱時未固溶的MC碳化物係變為微細且均勻,具有可 有效地抑制結晶粒成長之作用。另一方面,批碳化物係 硬質,會成為使切削性降低之原因。因此,在本發明, 藉由在切削加工時的工具表面形成上述的複合潤滑保護 皮膜,即便在鋼坯料中形成大量的MC碳化物亦能夠確保 良好的切削性之方面’具有重要的特徵。但是添加過量 的V,過剩地形成粗大的MC碳化物亦使冷作工具鋼的韌 性降低。因此,添加V時,較佳為i 〇%以下,更佳為〇 7% 以下。 •較佳是Nb : 0.5%以下Cu is an effect of increasing the hardness of steel when it is precipitated as e_Cu during tempering at the time of quenching and tempering. However, the Cu system causes a thermal brittleness of the steel billet. Therefore, it is preferable that the Cu system of the present invention is added in an amount of 丨〇% or less. Fork, because the brittleness of Cu can be suppressed by adding about the same amount, the cold working tool steel of the present invention can reduce the limit value according to the amount of ?12-201250010 when containing Ni. Preferably, V: 1. 〇% or less V forms various carbides and has an effect of increasing the hardness of the steel. Further, the formed un-solidified MC carbide system has an effect of suppressing the growth of crystal grains. Further, in particular, by adding in combination with the latter, the MC carbide which is not solid-solved at the time of quenching heating is fine and uniform, and has an effect of effectively suppressing the growth of crystal grains. On the other hand, the batch carbide is hard, which causes a decrease in machinability. Therefore, in the present invention, by forming the above-described composite lubricating protective film on the surface of the tool during the cutting process, it is important to ensure good machinability even if a large amount of MC carbide is formed in the steel blank. However, by adding an excessive amount of V, excessive formation of coarse MC carbides also lowers the toughness of the cold-work tool steel. Therefore, when V is added, it is preferably i 〇 % or less, more preferably 〇 7% or less. • preferably Nb: 0.5% or less
Nb係形成MC碳化物而具有抑制結晶粒的粗大化之 作用。但是過量地添加時,粗大的MC碳化物係過剩地形 成,使鋼的勃性降低。因此,添加時,較佳為〇5%以下 ’更佳為0.3 %以下。 而且,本發明係具有以下的特徵:將由上述成分構 成之冷作工具鋼調質成為58〜62HRC的硬度之後進行切 削加工。關於本發明之冷作工具鋼,係能夠藉由淬火回 火而安定地得到58HRC以上的調質硬度。亦能夠達成 60HRC以上的硬度。而且,在該高硬度狀態,因為具有 優異的切肖,卜险’不必特意在退火狀態進行切削加工之後 -13- 201250010 ,進行淬 火係能夠 接淬火。 退火後的 。因此, 硬鋼,能 後完成切 等。又, 度以外之 的上限設 火回火。或是 適用利用將鋼 而且,即便是 淬火之情況同 關於本發明之 夠免除起因於 削加工及進— 本發明為了亦 機械特性及安 為 62HRC。 因為不必 鬼熱作加 適用該直 樣地能夠 冷作工具 調質之熱 步有關於 能夠充分 定地進行 經過退 工之後 接淬火 得到改 鋼,係 處理變 坯料的 地維持 切削加 火狀態 的冷卻 的情況 善切削 藉由使 形,亦 製造之 冷作工 工,將 本身,淬 過程之直 ’與適用 性之效果 用作為預 能省略最 退火步驟 具鋼的硬 調質硬度 又雖然包含本發明的冷作加工用模具的製造方法 之模具’係具有優異的尺寸精確度耐摩耗性,藉由進行 表面PVD處理,在維掊;t; p ή ^ 声行阿尺寸精確度之同時,亦能夠進 一步提升耐摩耗性。 [實施例] 使用高頻感應熔融爐將材料熔解,來製造具有表1 所表示的化學成分之鋼塊。接著,對該等進行使锻造比 成為10左右之熱作锻造,冷卻後,於860 °c進行退火。隨 後’對該等退火材料進行從之藉由空氣冷卻的淬 火處理之後’於500~540°c下藉由2次的回火處理,而調 質成為60HRC的目標硬度’製造用於評價切削性之試片 201250010 備考 本發明例 1 1 比較例 1 1 1 ! i 1硬度 1 (HRC) VO S KTi S Os S s s 卜 o v〇 卜 〇\ 卜 σ\ On S oo S oo 〇 v〇 § oo o VO s S cs s 寸 s 寸 s OO 3 oo cK p s 寸 σ\ in On σ; «—H s <N s 〇 <N S On iT) o S 成分組成(mass%) d PQ PQ d PQ PQ d PQ d PQ d PQ d PQ d PQ d PQ d CQ PQ d PQ d CQ d m PQ OQ d PQ d CQ m d PQ d PQ d PQ d PQ PQ d PQ d PQ 1ά CQ PQ eN o cs o (N 〇 (S o o (N d> o o V V o V o V o r-H d V r»H o V O V o o ro »—H o T—K o (N d (N 〇 (N 〇 (N d <N o o <N 〇 f—H o o ΙΛ o 〇 I 0.059 I 0.070 I 0.099 | | 0.117 | 0.107 | | 0.250 | I 0.190 | 1 ο.ικΠ I 0.140 | I 0.090 I | 0.065 | | 0.230 | | 0.047 | | 0.075 | | 0.111 | [0.007 | I 0.016 I o.oio | 1 o.oii 1 | 0.012 | 0.021 | 0.012 | | 0.016 | 1 0.014 | | 0.009 | 0.027 1 o.ioo | 1 o.ioo | 0.094 0.170 (3 o o V o o »-H o V T—H o V r-H d V r-H o o 〇 V o d V o d V o o o »-H o V O T—S d V o o V o d V 寸 cn o o o o o o > v〇 <N 〇 CN O CN o cs o H o v〇 CN 〇 (N 〇 o » < o Γ·" Ή o o *—H d V o o o o (N o d V〇 (N 〇 CN 〇 o m <N 〇 to CN 〇 cs o 艺· o S o 〇\ <N 〇 VO (N o ^Ti <N o V〇 <N 〇 吞 o 00 »T) o 〇 I〇 吞 o (N »〇 rs* v〇 o cs o S; o r-j OS as o 〇 σ\ o 00 as o 00 Os o ° »·^ ON ON 〇 oo Os 〇 s s v〇 On 〇 s !〇 r-H s; o o T-H o V »—H o V r—1 o V r-H o V o o V cn v〇 O o V o r—H o V o V 寸 d (N d o V r-H o o V o V o V d V r*H o V 〇 o o o V o o o o V o o CO l> 00 VO 00 VO l> 卜^ 〇\ 00 vd S S oo V〇 »n oo m »ri 寸 寸 (S wS Os uS cs 00 l> v〇 ON uS s \n s On v〇 v〇 ON vd s 寸 寸· CN 寸· v〇 On *ri § u-> v〇 <N v〇 o (N 卜 cs o H o V o o V o o o V o V 〇 V o <N o <s o o o V 〇 o o V o o o r-H o o o V ο r—H o 〇 〇 o V o o o T—H o 00 | 0.0530 | 0.0554 | I 0.0581 I 0.0610 0.0542 | 0.0563 | | 0.0554 ] | 0.0821 | | 0.0483 | 0.0626 0.0450 0.0820 I 0.0815 | 0.0772 1 0.0626 I 0.0014 1 0.0610 | 0.0600 | I 0.0580 | 1 0.0600 | 1 0.0575 | 0.0585 1 0.0550 1 0.0570 | 0.0060 | | 0.0624 | | 0.0025 | 0.0298 | 0.0550 0.0529 Ρη | 0.004 | 0.006 | I 0.006 | 0.025 | 0.028 | | 0.025 | | 0.024 | 1 0.027 | | 0.025 i I 0.025 | | 0.027 | I 0.025 I I 0.026 I I 0.025 I I 0.026 I 0.005 I 0.0041 I 0.005 | I 0.006 J I 0.006 I 0.008 I 0.008 1 I 0.007 1 I 0.008 I I 0.027 I 1 0.028 I I 0.024 I I 0.025 I I 0.026 I | 0.026 | a s o τ«Ή t—H m oo o 00 On d s σ\ On C\ 〇 o 卜 o o g o o s r-H v〇 On O o CN OO o σ; o ν〇 OO ο 00 o o 对 o o o i—H t-H s 00 〇 芝· oo On <N as »—H r-H <N 〇\ O) T-H s (N oi 0 01 CS (N <N On 〇\ On 〇 O) 1—H o <N r4 O) m ΚΠ T—< *Τ) τ—Η ON 〇 00 <N o o o <N τ-Ή «•H r-H u I 0.800 I 0.785 I 0.773 I I 0.820 0.706 | 0.770 I I 0.782 | I 1.012 I I 0.626 I I 0.626 1 | 0.757 I I 0.632 I I 0.657 I I 0.655 I I 0.607 ! I 0.760 I I 0.770 I I 0.819 I | 0.804 I | 0.810 I I 1.020 | I 0.997 I I 1.016 1 I 1.015 I I 0.580 I I 0.765 I I 0.771 I 1 0.765 1 I 0.957 I 1.120 实ό (N ΓΟ 寸 v〇 卜 OO On o T-H c>j cO 寸 jq a m m m \n m 201250010 切削性試驗係使用日立TOOLS股份有限公司製刀片 PICOmini作為對應高硬度材料的切削之刀鋒交換式工具 藉由平面切削來實施。刀片(insert)係將超硬合金作為基 料且在表面施加TiN塗覆者。切削條件係切削速度為 70m/min、轉速為1857/min、輸送速度為743mm/min、每 一刀刃的輸送量〇 4mm/刀刃、切入深度為〇. 1 5mm、切入 寬度為6mm、刀刃數為1。 切削性試驗基於以下2點而進行,首先,評價在切削 工具表面之包含Ai2〇3及MnS之複合潤滑保護皮膜的形 成量。該形成量係在切削剛開始後之切削距離為〇 8m的 階段,從切削面(cutting face)側使用ΕΡΜΑ分析刀片作為 此時之A1及s的平均統計數。然後,將切削距離延長至8m 而使用光學顯微鏡實測此時的工具摩耗量。將該等的評 價結果顯示在表2。 -16- 201250010 [表21 試料 No. A1平均統計數 S平均統計數 工具摩耗量 (mm) 備考 1 158 57 0.066 本發明例 2 152 59 0.068 3 167 50 0.065 4 171 53 0.060 5 153 69 0.040 6 184 44 0.062 7 155 41 0.062 8 110 41 0.052 9 162 111 0.048 10 153 96 0.046 11 125 77 0.049 12 145 104 0.044 13 90 70 0.064 14 106 71 0.051 15 138 122 0.058 21 8 3 0.429 比較例 22 57 9 0.106 23 28 8 0.194 24 19 5 0.071 25 45 7 0.282 26 86 24 0.082 27 37 9 0.106 28 57 26 0.112 29 77 10 0.235 30 7 3 0.100 31 87 8 0.547 32 64 3 0.126 33 101 22 0.118 34 110 39 0.091 35 109 25 0.130 有關於本發明之冷作工具鋼的切削加工,係在切削 工具表面形成複合潤滑保護皮膜,而能夠抑制工具摩耗 。而且,即便添加有形成未固溶碳化物之N b和V之情況 ,亦能夠維持良好的切削性。 相對於此,相較於本發明,未滿足本發明之冷作工 具鋼的切削加工係工具摩耗量大。 -17- 201250010 第1圖係顯示在試料No.3、5、15、22、30所使用之 切削工具的刀腹面(flank face)及切削面之數位顯微鏡照 片,第2圖係對應該部分之使用上述的ΕΡΜΑ之分析結果( 各元素的高濃度部分係以淡色顯示)。在表2,Α1及S的平 均統計數高之試料No.3 ' 5、15係在第2圖的ΕΡΜΑ分析亦 能夠確認Α1及S大量地附著在工具的廣闊範圍《與此相較 ,冷作工具鋼的Α1量為較低之試料ν〇·22,Α1及S的平均 統計數亦較試料No.3、5、15低,Α1和S的附著範圍亦狹 窄。又’原來鋼中的A1及S含量即較低之試料No.30,該 等元素的平均統計數亦較低,且使用ΕΡΜΑ分析係幾乎無 法檢出Α1及S (能夠檢出的’大部分被認為是從試片轉移 之Fe及Cr)。 而且,顯示切削工具的摩耗狀態之第1圖,對應於上 述的結果’在試料No. 3、5、1 5的工具切削面,係顯著地 附著有附著物,得知工具摩耗係在刀腹面及切削面的雙 方均被抑制。又,工具摩耗係均勻且安定地進行。相對 於此,試料No.22的工具摩耗量係接近N〇 3的二倍且在工 具亦產生破片。而且在試料Νο·3〇的工具表面係亦與試料 Ν 〇. 2 2同樣地,損傷嚴重。 再者’第3圖係將在試料ν〇·3、22、30的工具表面確 認之附著物,與位於在其下面之TiN塗覆同時顯示之剖面 TEM影像。符合上述的結果,仍然是刈及s的平均統計數 較高的試料No.3的附著物係較厚,隨著入丨及s的平均統計 數變低,試料No.22的附著物係轉變為較薄。試料n〇3〇 係幾乎無法觀察到附著物。而且,與Ν〇·3同樣,在試料 •18- 201250010 Νο·22的工具表面亦附著有Al2〇3及MnS,但是其厚度係 較薄且如上述產生破片。試料N 〇. 3的附著物係發揮高潤 滑保護功能,可從以下得知:由於切削加工時的摩擦應 力,通常會產生塑性變形之工具表面的TiN塗覆,在附著 物較厚的試料No.3係被抑制(塑性變形區域為最狹窄)。 【圖式簡單說明】 第1圖係顯示在本發明及比較例的切削加工所使用 之切削工具的刀腹面及切削面之數位顯微鏡照片。 第2圖係將在第1圖的切削工具的表面所形成之附著 物以ΕΡΜΑ(電子探針微分析器)分析時之彩色圖。 第3圖係將第2圖的附著物與TiN塗覆同時顯示之剖 面TEM(透射型電子顯微鏡)照片。 【主要元件符號說明】 1 用以調製試料之保護膜 2 切削時的附著物 3 TiN塑性變形區域 4 TiN未變形區域 -19-Nb forms MC carbide and has an effect of suppressing coarsening of crystal grains. However, when it is excessively added, coarse MC carbides are excessively formed to lower the boring property of the steel. Therefore, when added, it is preferably 5% or less ‘more preferably 0.3% or less. Further, the present invention is characterized in that the cold-work tool steel composed of the above components is tempered to have a hardness of 58 to 62 HRC, and then subjected to a cutting process. Regarding the cold-work tool steel of the present invention, it is possible to stably obtain a quenched and tempered hardness of 58 HRC or more by quenching and tempering. It is also possible to achieve a hardness of 60 HRC or more. Further, in this high-hardness state, since it has an excellent cut-off, it is not necessary to perform the cutting process in the annealed state -13-201250010, and the quenching system can be quenched. After annealing. Therefore, hard steel can be cut after completion. In addition, the upper limit of the degree is set to temper. Or it is suitable to use steel and even if it is quenched, it is exempt from the invention and is caused by cutting and further. The present invention is also intended to have mechanical properties and safety of 62HRC. Because it is not necessary to use the hot work and apply the direct sample, the hot step of the cold working tool can be adjusted to be able to fully perform the quenching after the retreat and obtain the steel, and the cooling of the cutting material is maintained. The situation of good cutting by the shape, also made by the cold workman, the self, the straightening of the quenching process and the applicability effect as the pre-emption of the hardening hardness of the steel in the most annealing step, although including the invention The mold for manufacturing the mold for cold working has excellent dimensional accuracy and wear resistance. By performing surface PVD treatment, it is possible to further improve the dimensional accuracy of the 掊 ;; t; p ή ^ sound line. Improve wear resistance. [Examples] A steel block having the chemical composition shown in Table 1 was produced by melting a material using a high frequency induction melting furnace. Next, the forging ratio was set to about 10 for hot forging, and after cooling, annealing was performed at 860 °C. Subsequently, after the quenching treatment of the annealed material by air cooling is performed, the tempering is performed at 500 to 540 ° C twice, and the quenching is changed to a target hardness of 60 HRC. Test piece 201250010 Preparation of the present invention Example 1 1 Comparative example 1 1 1 ! i 1 hardness 1 (HRC) VO S KTi S Os S ss ov 〇 〇 〇 卜 〇 〇 oo oo oo VO s S cs s inch s inch s OO 3 oo cK ps inch σ\ in On σ; «—H s <N s 〇<NS On iT) o S component composition (mass%) d PQ PQ d PQ PQ d PQ d PQ d PQ d PQ d PQ d PQ d CQ PQ d PQ d CQ dm PQ OQ d PQ d CQ md PQ d PQ d PQ d PQ PQ d PQ d PQ 1ά CQ PQ eN o cs o (N 〇( S oo (N d > oo VV o V o V o rH d V r»H o VOV oo ro »—H o T—K o (N d (N 〇(N &(N d <N oo <N 〇f—H oo ΙΛ o 〇I 0.059 I 0.070 I 0.099 | | 0.117 | 0.107 | | 0.250 | I 0.190 | 1 ο.ικΠ I 0.140 | I 0.090 I | 0.065 | | 0.230 | | 0.047 | | 0.075 | | 0.111 [0.007 | I 0.016 I o.oio | 1 o.oii 1 | 0.012 | 0.021 | 0.012 | | 0.016 | 1 0.014 | | 0.009 | 0.027 1 o.ioo | 1 o.ioo | 0.094 0.170 (3 oo V oo »-H o VT—H o V rH d V rH oo 〇V od V od V ooo »-H o VOT—S d V Oo V od V inch cn oooooo >v〇<N 〇CN O CN o cs o H ov〇CN 〇(N 〇o » < o Γ·" Ή oo *—H d V oooo (N od V 〇(N 〇CN 〇om <N 〇to CN 〇cs o 艺· o S o 〇\ <N 〇VO (N o ^Ti <N o V〇<N 〇 oo 00 »T) o 〇I〇 o o (N »〇rs* v〇o cs o S; o rj OS as o 〇σ\ o 00 as o 00 Os o ° »·^ ON ON 〇oo Os 〇ssv〇On 〇s !〇 rH s; oo TH o V »—H o V r—1 o V rH o V oo V cn v〇O o V or—H o V o V 寸 d (N do V rH oo V o V o V d V r*H o V 〇ooo V oooo V oo CO l> 00 VO 00 VO l> 卜^ 〇\ 00 vd SS oo V〇»n oo m »ri inch (S wS Os uS cs 00 l> v〇ON uS s \ns On v〇v〇ON vd s inch inch · CN inch · v〇On *ri § u->v〇<N v〇o (N 卜 c o H o V oo V ooo V o V 〇V o <N o <sooo V 〇oo V ooo rH ooo V ο r—H o 〇〇o V ooo T—H o 00 | 0.0530 | 0.0554 | I 0.0581 I 0.0610 0.0542 | 0.0563 | | 0.0554 ] | 0.0821 | | 0.0483 | 0.0626 0.0450 0.0820 I 0.0815 | 0.0772 1 0.0626 I 0.0014 1 0.0610 | 0.0600 | I 0.0580 | 1 0.0600 | 1 0.0575 | 0.0585 1 0.0550 1 0.0570 | 0.0060 | | 0.0624 | | 0.0025 | 0.0298 | 0.0550 0.0529 Ρη | 0.004 | 0.006 | I 0.006 | 0.025 | 0.028 | | 0.025 | 0.024 | 1 0.027 | | 0.025 i I 0.025 | | 0.027 | I 0.025 II 0.026 II 0.025 II 0.026 I 0.005 I 0.0041 I 0.005 | I 0.006 JI 0.006 I 0.008 I 0.008 1 I 0.007 1 I 0.008 II 0.027 I 1 0.028 II 0.024 II 0.025 II 0.026 I | 0.026 | aso τ«Ή t—H m oo o 00 On ds σ\ On C\ 〇o oogoos rH v〇On O o CN OO o σ; o ν〇OO ο 00 oo for oooi —H tH s 00 〇芝· oo On <N as »—H rH <N 〇\ O) TH s (N oi 0 01 CS (N <N On 〇\ On 〇O) 1—H o < ;N r4 O) m ΚΠ T—< *Τ) τ—Η ON 〇00 <N ooo <N τ-Ή «•H rH u I 0.800 I 0.785 I 0.773 II 0.820 0.706 | 0.770 II 0.782 I I I I I I I I I I I I I I I I I I I I I I I 0.765 II 0.771 I 1 0.765 1 I 0.957 I 1.120 ό (N ΓΟ 〇 v 〇 OO On o TH c gt; j cO inch jq ammm \nm 201250010 Machinability test using Hitachi TOOLS Co., Ltd. blade PICOmini as the corresponding high The cutting edge exchange tool for the hardness material is implemented by plane cutting. The insert uses a superhard alloy as a binder and applies a TiN coater to the surface. The cutting conditions are cutting speed 70m/min, rotation speed 1857/min, conveying speed 743mm/min, conveying capacity per blade 〇4mm/blade, cutting depth 〇. 1 5mm, cutting width 6mm, number of cutting edges 1. The machinability test was carried out based on the following two points. First, the amount of the composite lubricating protective film containing Ai2〇3 and MnS on the surface of the cutting tool was evaluated. This formation amount is a stage in which the cutting distance immediately after the start of cutting is 〇 8 m, and the ΕΡΜΑ analysis blade is used as the average statistic of A1 and s at this time from the cutting face side. Then, the cutting distance was extended to 8 m, and the tool wear amount at this time was measured using an optical microscope. The evaluation results of these are shown in Table 2. -16- 201250010 [Table 21 Sample No. A1 Average Statistics S Average Statistics Tool Wear (mm) Remarks 1 158 57 0.066 Inventive Example 2 152 59 0.068 3 167 50 0.065 4 171 53 0.060 5 153 69 0.040 6 184 44 0.062 7 155 41 0.062 8 110 41 0.052 9 162 111 0.048 10 153 96 0.046 11 125 77 0.049 12 145 104 0.044 13 90 70 0.064 14 106 71 0.051 15 138 122 0.058 21 8 3 0.429 Comparative example 22 57 9 0.106 23 28 8 0.194 24 19 5 0.071 25 45 7 0.282 26 86 24 0.082 27 37 9 0.106 28 57 26 0.112 29 77 10 0.235 30 7 3 0.100 31 87 8 0.547 32 64 3 0.126 33 101 22 0.118 34 110 39 0.091 35 109 25 0.130 The cutting process of the cold-work tool steel of the present invention forms a composite lubrication protective film on the surface of the cutting tool, and the tool wear can be suppressed. Further, even when Nb and V which form undissolved carbides are added, good machinability can be maintained. On the other hand, compared with the present invention, the cutting tool of the cold working tool steel which does not satisfy the present invention has a large amount of wear. -17- 201250010 Fig. 1 shows a digital microscope photograph of the flank face and the cutting surface of the cutting tool used in samples No. 3, 5, 15, 22, and 30. Fig. 2 is a partial view. The analysis results of the above enthalpy were used (the high concentration portion of each element is shown in a pale color). In Table 2, the sample No. 3 '5, 15 with a high average number of Α1 and S is also analyzed in the second figure. It can be confirmed that Α1 and S are attached to a wide range of tools in a large amount. The amount of Α1 of the tool steel was lower than that of the sample ν〇·22, and the average statistic of Α1 and S was also lower than that of the samples No. 3, 5, and 15, and the adhesion range of Α1 and S was also narrow. Also, 'the raw material No. 30 in which the A1 and S contents in the original steel are lower, the average statistic of these elements is also low, and the ΕΡΜΑ analysis system is almost impossible to detect Α1 and S (the most part that can be detected) It is considered to be Fe and Cr transferred from the test piece. In addition, the first graph showing the wear state of the cutting tool corresponds to the above-described result. In the tool cutting faces of Sample Nos. 3, 5, and 15 , the deposits were remarkably attached, and the tool wear was found on the flank. Both sides of the cutting surface are suppressed. Moreover, the tool wear is performed uniformly and stably. On the other hand, the tool No. 22 had a tool wear amount close to twice the N〇 3 and a fragment was generated in the tool. Moreover, the surface of the tool of the sample Νο·3〇 was also severely damaged as in the sample Ν 〇. 2 2 . Further, Fig. 3 is a cross-sectional TEM image showing the adhering matter confirmed on the surface of the sample of the samples ν〇·3, 22, and 30 simultaneously with the TiN coating under the coating. In accordance with the above results, the sample No. 3 with a higher average statistic of 刈 and s is thicker, and the average number of enthalpy and s is lower, and the attachment of sample No. 22 is changed. It is thinner. The sample was almost invisible to the n〇3〇 system. Further, similarly to Ν〇·3, Al2〇3 and MnS were adhered to the surface of the tool of the sample 18-201250010 Νο·22, but the thickness thereof was thin and the fragments were generated as described above. The attached material of the sample N 〇. 3 exhibits a high lubrication protection function, and it can be known from the following that TiN coating on the surface of the tool which is usually plastically deformed due to the frictional stress during the cutting process, and the sample No. which is thick in the attached material The .3 system is suppressed (the plastic deformation zone is the narrowest). BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a digital microscope photograph showing a flank face and a cutting face of a cutting tool used in the cutting process of the present invention and a comparative example. Fig. 2 is a color diagram when the deposit formed on the surface of the cutting tool of Fig. 1 is analyzed by a crucible (electron probe microanalyzer). Fig. 3 is a cross-sectional TEM (transmission electron microscope) photograph showing the attachment of Fig. 2 together with TiN coating. [Explanation of main component symbols] 1 Protective film for modulating the sample 2 Attachment during cutting 3 TiN plastic deformation zone 4 TiN undeformed zone -19-
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CN103834872A (en) * | 2012-11-26 | 2014-06-04 | 天工爱和特钢有限公司 | Die steel with high-wearing resistance |
JP6032582B2 (en) * | 2013-03-29 | 2016-11-30 | 日立金属株式会社 | Manufacturing method of steel material for mold |
EP3199656B1 (en) * | 2014-09-26 | 2019-04-10 | Hitachi Metals, Ltd. | Cold work tool material and method for manufacturing cold work tool |
JP6519226B2 (en) * | 2015-02-26 | 2019-05-29 | 大同特殊鋼株式会社 | Alloy tool steel |
JP6137428B2 (en) * | 2015-03-26 | 2017-05-31 | 日立金属株式会社 | Cold tool and manufacturing method thereof |
EP3305934B1 (en) | 2016-03-18 | 2020-02-19 | Hitachi Metals, Ltd. | Cold working tool material and cold working tool manufacturing method |
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