TW201250011A

TW201250011A - Hot work tool steel with superior toughness and method for manufacturing the same

Info

Publication number: TW201250011A
Application number: TW101106849A
Authority: TW
Inventors: Kouta Kataoka; Yousuke Nakano
Original assignee: Hitachi Metals Ltd
Priority date: 2011-03-03
Filing date: 2012-03-02
Publication date: 2012-12-16
Also published as: TWI447237B; WO2012118053A1; EP2682491A1; EP2682491A4; CN103403209B; EP2682491B1; CN103403209A

Abstract

The present invention provides toughness improved hot work tool steel and method for manufacturing the same. The hot work tool steel is containing C: 0.3 to less than 0.6%, Si: 1.5% or less, Mn: 1.5% or less, Cr: 3.0 to less than 6.0%, Zn: exceeding 0.0025 to 0.025%, and P: 0.005% or more in mass %, moreover, Zn / P of the hot work tool steel is exceeding 0.5. Furthermore, the method for manufacturing the hot work tool steel includes: the first step to obtain ingredient composition containing P of 0.005 mass% or more of hot work tool steel of molten steel; the second step to add Zn to the aforementioned ingredient composition of hot work tool steel of molten steel; and the third step to obtain a steel ingot by casting the aforementioned Zn added molten steel. Among the steps of method for manufacturing the hot work tool steel, the second step is adding Zn to make the composition of steel block after casting in the third step for containing Zn: exceeding 0.0025 to 0.025 mass%, P: 0.005 mass% or more, and Zn / P: exceeding 0.5.

Description

201250011 六、發明說明：【發明所屬之技術領域] 本發明係、關於t適合供用於加壓金屬μ或鍛造金屬模具、壓鑄模具、壓出工具等多種的熱作工具之已提高韌性之熱作工具鋼及其製造方法。【先前技術】熱作工具係由於一邊與高溫的被加工材或硬質的被加工材接觸而被使用，必須兼具耐得住熱疲勞或衝擊的強度與韌性。因此，以往於熱作工具的領域所用的鋼種（以下稱為熱作工具鋼）中，係使用例如JIS鋼種的SKD6i 系之合金工具鋼。而且，有提案重新估計構成熱作工具鋼的主要元素之添加量，進一步規制管理AS、Bi、Sn、 Zn、Sb等的多種雜質，而提高熱作工具鋼的韌性之手法 (參照專利文獻1)。然而，將多種的雜質元素調整至各別所規定的範圍内’係會與製造成本的提高有關聯。相對於此，本發明者不藉由高價且特殊的元素之添加，而對於鐵鋼材料的領域中作為合金未曾被積極添加的元素，進行專心致力的調査，結果發現藉由以指定含量的範圍添加以往作為雜質處理的Zn，可大幅改善知性丨、參照專利文獻2)。即，以質量％計含有c: 0.3〜低於0.55% 、S i : 1.5 % 以下、Mn : 1 · 5 % 以下、Cr : 3 . 〇〇〜5 · 6 5 % 之熱作工具鋼，Zn : 0.001〜〇.〇 15%之熱作工具鋼。先前技術文獻專利文獻專利文獻1 特開2003- 1 55540號公報專利文獻2 特開2007-2244 1 8號公報 201250011 題] I案的Ζη添加之技術’係有效作為提生之新手法。而且’藉由利用專利文 1錢了 Ζη的鋼廢料當作再生原料，亦诗。本發明者著眼於藉由此積極的Ζη 其它雜質元素所致南此等雜質元素的量會增加的雜質含於去除雜質的能量製造過程中對環境境負荷的韌性優異【發明内容】 [發明所欲解決的問專利文獻2所：高熱作工具鋼的韌獻2的手法，可活戶適合於減輕環境負添加而提高韌性之的韌性劣化之可能容許量，可一邊增量多之低級廢料的使用量，可進一步所造成的負荷。本發明之目的之熱作工具鋼及其 [解決問題的手段] 本發明者調查及環境造成的影響係大幅降低熱作工耗費的能量大，基料的使用，係對於低此之環境負荷，分的韌性之手法。性之劣化，係可藉 2: η來彌補。而且，具體之Ρ與Ζη的Β 成分調整的手法明效果，檢討可彌補性。若可適當地提加被預料今後排出使用率，而減低用減低熱作工具鋼的在於提供可減輕環製造方法。熱作工具鋼中所含。結果得到以下見具鋼的韌性之元素於此等的理由，而環境的負荷大之元檢討即使提高ρ的結果，查明了 ρ含由添加相對於該ρ 隨著可充分利用此 1係量，Θ時使達成確，而達成本發明有雜質元素對韌性解：尤其是Ρ(磷），而且於去除時所如滯了促進低級廢素。於此，為了降容許量也可維持充量的增加所致的韌含量而言適當量的韌性之補充效果的該關係量的適合之 201250011 即，本發明為以質量％計，含有C : 0.3〜低於0.6% 、Si : 1.5%以下、Μη : 1.5%以下、Cr : 3.0〜低於 6.0%之熱作工具鋼，其特徵為：Zn:超過0.0025〜0.025%，P : 0.005%以上’而且Zn/P :超過0.5之韌性優異之熱作工具鋼。較佳為P : 〇. 〇丨％以上。而且按照需要，可含有 Mo及W以單獨或複合為（m〇 + 1/2W) : 3.5%以下，或可更含有V : 1.5 %以下。具體地，以質量％計，C : 0.3〜低於0.6%，Si : 1.5% 以下，Mn : 1.5 %以下，Ni : 1.5 %以下（包含〇%)，Cr : 3.0〜低於6.0 % ’ Mo及W係以單獨或複合為（m〇 + 1 /2 W): 3 · 5 % 以下 ’ V : 1.5%以下 ’ Nb : 0.3%以下（包含〇%)，c〇 : 5.0% 以下（包含 0%)，Zn :超過〇〇〇25〜〇〇25%，p : 〇〇〇5〇/〇以上，而且Zn/P :超過〇·5，包含剩餘部分之以及無可避免的雜質之韌性優異之熱作工具鋼。較佳為p: 〇〇1% 以上。造方法，之熱作工熱作工具將前述添其中前述塊的成分 p : 0.005 鋼的方式的成分組 +货月马韌性優異之熱作工具鋼之製其特徵為包含：得到含有G.0G5質量％以上的p ::的成分組成之熔鋼之第i步驟’與於前述加右成分組成之熔鋼中添加Zn之第2步驟，與篦Zn的炼鋼鎿造而得到鋼塊之第3步驟，且步驟係以使前述Μ楚1 _ μ ▲主組成成為人右/之的第3步驟的矯造後之鋼質量。過0·0025〜°·025質量％、，添加7，而且Zn/P:超過0·5《熱作工具 ,'' n。較佳為在前述第1步驟所得成以質量%計，含有W以上=鋼刖述第3 201250011 造後之鋼塊的成分組成係以質量％計，含有P : 〇〇 i %以上。又，較佳為前述鋼塊的成分組成係以質量V。計，含有 C : 0.3〜低於 0.6%、Si : 1.5%以下、Μη : 1.5。/0以下、 Cr : 3.0〜低於6.0%之熱作工具鋼。又，可按照需要，以單獨或複合含有Mo及W，（Mo + 1/2W) : 3.5%以下，或更含有V : 1.5 %以下。前述第3步驟的鑄造後之鋼塊的最典型之成分組成 ’係為以質量％計，C : 0.3〜低於0.6 %、S i : 1.5 %以下、 Μη : 1.5%以下、Ni : 1.5%以下（包含〇%)、Cr ·· 3 〇〜低於 6.0°/〇’1^〇及\\^係以單獨或複合，（1^〇 + 1/2\¥):3.5%以下，V ·· 1.5%以下 ' Nb ·· 0.3%以下（包含 0%)、c〇 : 5 〇% 以下（包含 0%)、Ζη.超過 0.0025 〜〇·〇25%、P: 〇〇〇5% 以上’而且Zn/P:超過0.5’並包含剩餘部分之p>e及無可避免的雜質之熱作工具鋼。較佳為p : . 〇 1 %以上。 [發明的效果] 依照本發明，由於即使不將熱作工具鋼中所含有的 P作為雜質管理在極低值’也可維持充分的勒性，故可節約為了低P化的能量消耗量’可減輕對環境的負荷。而且’用於維持充分的勃性之Zn量，藉由本發明的添加手法’而可恰當的調整。根據以上，本發明可飛快地改善熱作工具鋼的韌性，對於可適用於多種多樣的用途· 環境之熱作工具鋼的實用化’係為有效的技術。【實施方式】 [實施發明的形態] 201250011 本發明，積極地添本發明的添含有大幅降鋼，若利用可發揮其提多的以往必定中，可削生利用。再的能量及時鋼之成分限 • Zn :超過韌性使與容許工具，也容許的選的再需要工具的大特徵在於為了提高熱作工具鋼的力以往作為雜質處理的Zn。而且，藉由加Zn量之關係明確，而在特定的範圍内低韌，性的元素之P。即，發現對於熱作 Zn當作合金元素，則即使p的含量變多问韌性的效果。而且，由於本發明中可須極度極低化的P之含量，故在原材料減高級的低P廢料之使用量，適於廢料者，亦可減低精煉步驟中的p之去除所間。以下，說明關於本發明製造的熱作定的理由（關於質量％，僅記載為％)。 0.0025〜0.025% ^ Zn係對於本發明最重要的添加元素，藉由添加而顯者提高韌性。而且，藉由添加超過〇〇〇25%，可充分得到本效果。較佳為0.003%以上。另—方面，即使多添加其效果也會到達極限。再者，若過度添加而在粒界等發生極端的偏析，則此反而可能成為使靱性變差的主要原因又’由於添加技術亦會變繁雜，故使上限為〇〇 2 5 〇/〇。較佳為0.020%以下，更佳為〇〇15%以下。 p : 0.005% 以上 P係在回火等的熱處理時偏析在舊沃斯田鐵粒界而使粒界脆化之元素。因此，為了提高熱作工具鋼的韌性 ’通常係儘可能管理為低值之雜質元素。然而，於本發明中’由於以最大限度利用上述的Zn添加所致之韌性提旬效果’可彌補P所致的韌性之劣化部分。而且，因此 -8- 201250011 所需要的Zn添加之顯签紛里之p含量的Zn添加= = =調整相對於後述里而獲传。因此’本發明的埶作工且鋼可容許0.005%以上的^ ㈣…作工- ,,w p ... 量較佳為0.01 %以上，更201250011 VI. Description of the Invention: [Technical Field of the Invention] The present invention relates to a hot work for improving toughness of a hot working tool suitable for use in a pressurizing metal μ or a forged metal mold, a die-casting mold, an extrusion tool, and the like. Tool steel and its manufacturing method. [Prior Art] Since the hot working tool is used in contact with a high-temperature workpiece or a hard material to be processed, it is necessary to have both strength and toughness that can withstand thermal fatigue or impact. Therefore, in the steel type (hereinafter referred to as hot work tool steel) used in the field of hot working tools, for example, SKD6i alloy tool steel of JIS steel type is used. In addition, there is a proposal to re-estimate the amount of the main elements constituting the hot work tool steel, and further regulate the management of various impurities such as AS, Bi, Sn, Zn, and Sb, and improve the toughness of the hot work tool steel (refer to Patent Document 1). ). However, adjusting a plurality of impurity elements to the respective ranges specified is associated with an increase in manufacturing cost. On the other hand, the inventors of the present invention conducted an intensive investigation on an element which has not been actively added as an alloy in the field of iron steel materials by the addition of expensive and special elements, and found that by the specified content range Adding Zn which has been conventionally treated as an impurity can greatly improve the intellectual properties, and refer to Patent Document 2). That is, it contains c: 0.3 to less than 0.55%, S i : 1.5 % or less, Mn: 1 · 5 % or less, and Cr: 3 . 〇〇〜 5 · 6 5 % of hot work tool steel, Zn by mass% : 0.001 ~ 〇. 〇 15% of the hot work tool steel. CITATION LIST PATENT DOCUMENT Patent Document 1 JP-A-2003- 1 55 540 Patent Document 2 JP-A-2007-2244 No. 8 No. 201250011 The technique of adding Ζ in the case of I is effective as a new method of promotion. Moreover, by using the patented text, the steel scrap of Ζη is used as a raw material for recycling. The inventors of the present invention have focused on the fact that the amount of impurities such as the south which is increased by the positive Ζη other impurity element is increased in the energy production process for removing impurities, and the toughness against environmental load is excellent. [Invention] [Invention] Patent Document 2 to be solved: The method of toughness 2 of high-heating tool steel can be used to reduce the possibility of toughness deterioration of the environment and reduce the toughness of the toughness, and it is possible to increase the amount of low-grade waste at the same time. The amount of use can further increase the load. The hot work tool steel and the method for solving the problem of the present invention are inspected by the inventors and the influence of the environment is greatly reduced, and the energy consumption of the hot work is large, and the use of the base material is low for the environmental load. The method of resilience. The deterioration of sex can be compensated by 2: η. Moreover, the specific Ρ and Ζ Β 成分调整调整调整调整调整。。。。。。。。。。。。 If it is possible to appropriately increase the expected discharge rate in the future, and to reduce the use of the reduced-heat tool steel, it is possible to provide a method for reducing the loop manufacturing. Hot work tool steel is included. As a result, the following reasons for the toughness of the steel are obtained, and the environmental load is reviewed. Even if the result of ρ is increased, it is ascertained that the addition of ρ with respect to the ρ can be fully utilized. When the time is reached, the present invention has an impurity element for the toughness solution: especially bismuth (phosphorus), and the stagnation promotes the low-level waste. Here, in order to reduce the allowable amount, it is possible to maintain a suitable amount of the toughness due to an increase in the amount of charge, and the amount of the relationship of the toughness is suitable for 201250011. That is, the present invention contains C: 0.3 in mass%. ~ Hot work tool steel of less than 0.6%, Si: 1.5% or less, Μη: 1.5% or less, Cr: 3.0 to less than 6.0%, characterized by: Zn: more than 0.0025 to 0.025%, P: 0.005% or more' Further, Zn/P: a hot work tool steel having an excellent toughness of more than 0.5. Preferably, it is P: 〇. 〇丨% or more. Further, if necessary, Mo and W may be used alone or in combination (m〇 + 1/2W): 3.5% or less, or may further contain V: 1.5% or less. Specifically, C: 0.3 to less than 0.6%, Si: 1.5% or less, Mn: 1.5% or less, Ni: 1.5% or less (including 〇%), and Cr: 3.0 to less than 6.0% by mass % Mo And W system alone or in combination (m〇+ 1 /2 W): 3 · 5 % or less 'V : 1.5% or less ' Nb : 0.3% or less (including 〇%), c〇: 5.0% or less (including 0 %), Zn: more than 〇〇〇25~〇〇25%, p: 〇〇〇5〇/〇 or more, and Zn/P: more than 〇·5, excellent in toughness including the remaining part and inevitable impurities Hot work tool steel. Preferably, p: 〇〇 1% or more. The manufacturing method, the hot work hot working tool, is characterized in that the component of the above-mentioned block is a component of p: 0.005 steel, and the hot work tool steel having excellent toughness is included: the product contains: G.0G5 The second step of adding a Zn to the molten steel having the right component composition of the p:: component of the mass ratio or more and the second step of adding Zn to the molten steel having the right component composition, and the steel block of the 篦Zn is obtained. 3 steps, and the steps are the steel quality of the third step of making the aforementioned composition 1 _ μ ▲ main composition. After 0·0025~°·025 mass%, add 7, and Zn/P: more than 0. 5 "hot work tool, ''n. It is preferable that the component composition of the steel block after W3 or more is contained in the first step and contains W or more. The third component of the 20122012 process is contained in mass%, and contains P: 〇〇 i % or more. Further, it is preferable that the chemical composition of the steel block is a mass V. Including C: 0.3 to less than 0.6%, Si: 1.5% or less, and Μη: 1.5. /0 or less, Cr: 3.0 to less than 6.0% of hot work tool steel. Further, if necessary, Mo and W may be contained alone or in combination, (Mo + 1/2W): 3.5% or less, or more preferably V: 1.5% or less. The most typical component composition of the steel block after casting in the third step is % by mass, C: 0.3 to less than 0.6%, S i : 1.5% or less, Μη: 1.5% or less, and Ni: 1.5%. The following (including 〇%), Cr ·· 3 〇~ below 6.0°/〇'1^〇 and \\^ are separate or compound, (1^〇+ 1/2\¥): 3.5% or less, V ·· 1.5% or less ' Nb ·· 0.3% or less (including 0%), c〇: 5 〇% or less (including 0%), Ζη. More than 0.0025 〇〇〇 25%, P: 〇〇〇 5% or more 'And Zn/P: hot tool steel containing more than 0.5' and containing the remaining p>e and inevitable impurities. Preferably, it is p: . 〇 1% or more. [Effects of the Invention] According to the present invention, even if the P contained in the hot tool steel is not managed as an impurity at a very low value, sufficient sufficient performance can be maintained, so that energy consumption for low P can be saved. It can reduce the load on the environment. Further, the amount of Zn used to maintain sufficient boobility can be appropriately adjusted by the addition method of the present invention. According to the above, the present invention can quickly improve the toughness of the hot work tool steel, and is an effective technique for the practical use of hot work tool steel which can be applied to various applications and environments. [Embodiment] [Embodiment of the Invention] 201250011 The present invention is actively added to the present invention, and the addition of the steel is greatly reduced, and it is necessary to use it in advance. Re-intensity and timely steel composition limit • Zn: Exceeding the toughness and the allowable tool, and the allowable selection of the re-required tool is characterized by the fact that Zn is treated as an impurity in order to increase the force of the hot work tool steel. Moreover, the relationship between the amount of Zn and the amount of Zn is low, and the P of the element is low in a specific range. That is, it has been found that when hot Zn is used as an alloying element, the effect of toughness is increased even if the content of p is increased. Further, since the content of P which is extremely extremely low in the present invention can be extremely low, the amount of low-P waste used in the raw material is reduced, and it is suitable for the waste, and the removal of p in the refining step can be reduced. Hereinafter, the reason for the heat treatment of the production of the present invention (for the mass%, only %) will be described. 0.0025 to 0.025% ^ Zn is the most important additive element of the present invention, and the toughness is remarkably improved by the addition. Moreover, this effect can be fully obtained by adding more than 〇 25%. It is preferably 0.003% or more. On the other hand, even if you add more effects, you will reach the limit. Further, if excessive segregation occurs at the grain boundary or the like due to excessive addition, this may become a major cause of deterioration of the enthalpy. Further, the addition technique may become complicated, so the upper limit is 〇〇 2 5 〇 / 〇 . It is preferably 0.020% or less, more preferably 〇 15% or less. p : 0.005% or more P is an element which segregates in the old Worthfield iron grain boundary during heat treatment such as tempering to embrittle the grain boundary. Therefore, in order to improve the toughness of the hot work tool steel, it is usually managed as a low-value impurity element. However, in the present invention, the deterioration of the toughness due to P can be compensated for by the use of the above-mentioned toughness effect by Zn addition. Moreover, the Zn addition of the p content of the Zn addition required for -8-201250011 is === adjustment is transmitted with respect to the latter. Therefore, the work of the present invention and the steel can allow 0.005% or more of the work of -4, and the amount of wp is preferably 0.01% or more.

佳為即使在0.02%以上可維持充分㈣I • Zn/P :超過〇 5 於本發明的妖作τ目& & Ρ時，也必須要能確你即使含有0.005%以上的因此’必須調整相對於二之Ζη添加量。由使Zn/P之值超過0.5,可^伴之/；； =置。具體地，藉 :超過0.55。再者，超過保充刀的款性。較佳為Zn/P 以上的p，甚至β〇Λ ° ，的211/卩值，當含有〇·〇”/〇 -，心亦為較佳的條件。熱作工具鋼時，有 /足上述ρ與Ζη之關係的由各種的手法、成分調整之手法。即，藉含有上述的〜者，則：鑄；;時的溶鋼之成分組成調整成工具鋼之鋼塊，惟，令曰盾鑄造此，可得到本發明的熱作隨著時間的經過，自係、熔點低的揮發性元素，會溶鋼中應維㈣ζΛΐ中脫卜因此，對於鑄造時的添加的時間點之7 =，考慮上述的脫出量，將在熔鋼中造時炼鋼中的設定略多係、有效。’然而，控制將铸上述的脫出量之心調整至本發明的恰當值’而僅估計在此，於本發明；7 則再現性低’係難以達成。機調整，而事先調敕η係不在與其它添加元素相同的時量已決定的炼鋼作=作工具鋼的成分組成，以ρ含為止之經過時間，C的時機’可縮短至其後的鑄造變動。可抑制ζη的揮發等所致的Ζη/ρ比之 201250011 即係為’具體地包含：得到含有〇〇〇 5質量。以上的 ρ之熱作工具鋼的成分組成之熔鋼之第1步驟，與於前述熱作工具鋼的成分組成之熔鋼中添加Ζη之第2步驟，與將前述添加有Ζη的熔鋼鑄造而得到鋼塊之第3步驟。而且’在第2步驟中，係以第3步驟的鑄造後之鋼塊的成分組成成為含有Ζη:超過〇〇〇25〜〇〇25質量％、ρ: 0.005質量％以上，而且Ζη/ρ :超過〇·5之熱作工具鋼的方式’添加Ζη之熱作工具鋼之製造方法。前述第3步驟的鑄造後之鋼塊所含有的ρ較佳為〇〇丨質量％以上，更佳為0_02質量％以上。以下，說明關於各步驟。 •第1步驟：得到含有〇·〇〇5質量❶/。以上的P之熱作工具鋼的成分組成之溶鋼之步驟。藉由將熔鋼的成分組成調整為熱作工具鋼的組成’ 可將後述的第2步驟特化為主要來調整Ζη含量。而且，由於在添加指定量的Ζη後，可快速地轉移至後述的第3 步驟之鱗造’而容易恰當地調整鑄造後的鋼塊之Ζη含量再者’本發明的第1步驟之「得到熱作工具鋼的成分，’且成之溶鋼」，就是意味在後述的第2步驟之前，使成為已調正各種成分組成至熱作工具鋼之熔鋼的狀態。而且、時的成刀組成較佳為調整成為目標的鋼塊之成分組 ' 匕時依照接著添加Ζη時所使用的Ζη源之種類(成刀組成），若在Ζη添加的前後，成分組成會發生，動貝j較佳亦參考此變動量。因此’不限定於施予熔鲷、口金添加等之處理，例如亦可為準備溶解前的原枓之作業。而且，於溶解後，亦可施予去除介在物或雜 -10- 201250011 質的各種精煉處理。再者，第i步驟所得的p之含量較佳為〇.〇1質量％以上，更佳以上。 •第2步驟：於第.丨步驟的熱作工具鋼之j 之步驟。於本發明中，分開管理添加Zn的第2 1步驟，如上述係為重要。若將Zn添加於工具鋼的成分組成之熔鋼中，則易於調整七含量，而且可快速地轉移至後述的第3步者，本發明的第2步驟係不排除添加211以之處理。因此，此時關於Zn以外的元素種鋼塊之成分組成之間有若干的差異，只要精煉處理’亦可進行再度的微調整。 •第3步驟：將第2步驟的熔鋼鑄造而得〇藉由將經過第1及第2步驟的熔鋼鑄可溶製滿足本發明的成分組成之熱作工本發明的第3步驟之鑄造係不限於普通造連續鑄造法或其它特殊造塊法。本發明之藉由Zn添加的韌性提高效；咬化物多數分布，則被大幅阻礙其而變弱織中分布許多的碳化物之冷作工具鋼相比向效果通常在碳化物少的熱作工具鋼中之熔鋼所含有為〇‘〇2質量％容鋼中添加Zn 步驟與上述第預先5周整熱作〖目對於P之Zn 驟之缚造。再外之其它目的，若與目標的是不進行新的到鋼塊之步驟造而得到鋼塊具鋼。而且，塊法，亦可為民，若在組織中。即，與在組 ’上述的韌性被充分發揮。 201250011 因此，限定本發明的對象為钕作工如浐πς r ^ .、具鋼°熱作工具鋼例如h Jis-G_4404等中規定的 TTQ楚ΑΑ扣取之鋼。而且，除了 JIS專的規格鋼種，亦可適用於以細。μ、+、微故案的熱作工具鋼上述熱作工具鋼所規定的以外之 ffi. U, ^ . 素種，亦可視需要地添加。以下為本發明所製造執細忐。# % 、乍工具鋼的較佳成分組成拉說明關於數值限定的理由。 • C . 0 · 3 〜低於〇 6 0/。 C係一部分固溶於基體中而賦予形成碳化物而提古而十麻釭从4 ^ 強度’而一部为以固溶的侵入型原子之c，當與疋素。又，已換型；f + it % 4 與C親和性大的置換生席千共添加時，i(侵入 •，作為溶皙甩7 ’ s(置換型原子）效果，作馬岭貝原子的摩擦阻力而作度化的作用》惟，、A # ^. .亦可期待使鋼高強准過度的添加會導致知降低。因此，較佳π A 或…、作強度的。季乂佳“0.3〜低於。.6%’更佳為低於〇55% • Si : 1.5% 以下Good even if it is above 0.02%, it can maintain sufficient (4) I • Zn/P: When it exceeds 〇5 in the demon work of the present invention, it must be confirmed that even if it contains more than 0.005%, it must be adjusted. The amount added relative to the two. By setting the value of Zn/P to more than 0.5, it can be accompanied by /; Specifically, borrow: more than 0.55. Moreover, it exceeds the payment of the knife. Preferably, the 211/卩 value of p or even β〇Λ° above Zn/P, when containing 〇·〇”/〇-, is also a preferred condition. When hot tool steel, there is / The method of adjusting the relationship between ρ and Ζη by various methods and components. That is, by including the above-mentioned ~, then: casting;; the composition of the molten steel is adjusted to the steel block of the tool steel, but Therefore, it is possible to obtain a volatile element with a low melting point and a low melting point of the hot work of the present invention, and to remove the volatile element in the molten steel, and therefore, for the time point of the addition at the time of casting, 7 The amount of detachment is slightly more effective and effective in the steelmaking process in the molten steel. 'However, the control adjusts the above-mentioned amount of the amount of the detachment to the appropriate value of the present invention' and is only estimated here. In the present invention; 7 is low in reproducibility; it is difficult to achieve. The machine is adjusted, and the η system is not in the same amount as the other added elements, and the steel composition is determined as the composition of the tool steel. The elapsed time, the timing of C can be shortened to the subsequent casting changes. The ratio of Ζη/ρ ratio due to volatilization of ζη to 201250011 is specifically the first step of obtaining a molten steel containing a composition of 热5 mass or more of ρ hot work tool steel, and a second step of adding Mn to the molten steel having the composition of the hot work tool steel, and a third step of casting the molten steel to which Ζη is added to obtain a steel block. Further, in the second step, the second step is The composition of the steel block after casting in the third step is a method of containing Ζη: more than 〇〇〇25~〇〇25 mass%, ρ: 0.005 mass% or more, and Ζη/ρ: hot work tool steel exceeding 〇·5 The method of producing the hot-work tool steel to be added with Ζη. The ρ contained in the steel block after casting in the third step is preferably 〇〇丨% by mass or more, more preferably 0-02% by mass or more. Hereinafter, each step will be described. • Step 1: Obtain a step of melting steel containing the composition of the hot work tool steel of P·〇〇5 mass ❶/. above P. By adjusting the composition of the molten steel to the composition of the hot work tool steel' The second step described later can be specialized to adjust The content of Ζη. Moreover, since the 鳞η of the third step described later can be quickly transferred after adding a specified amount of Ζη, it is easy to appropriately adjust the Ζη content of the steel block after casting, and then the first step of the present invention. The phrase "the composition of the hot work tool steel, and the molten steel is formed" means that the composition of each component is adjusted to the molten steel of the hot work tool steel before the second step described later. In addition, the composition of the knives at the time is preferably adjusted to the target group of the steel block ' 匕 according to the type of Ζ η source used in the subsequent addition of Ζ η (the composition of the knives), and the composition of the composition before and after the addition of Ζη Occurs, and it is better to refer to this variation. Therefore, the treatment is not limited to the application of the melt, the addition of the gold, and the like, and may be, for example, an operation for preparing the original before the dissolution. Further, after the dissolution, various refining treatments for removing the intervening substance or the impurities of the -10-201250011 can be administered. Further, the content of p obtained in the i-th step is preferably 〇.〇1% by mass or more, more preferably more. • Step 2: The step of the hot work tool steel in step 丨. In the present invention, the second step of adding Zn is separately managed, and it is important as described above. If Zn is added to the molten steel of the composition of the tool steel, it is easy to adjust the seven contents, and it can be quickly transferred to the third step described later. The second step of the present invention does not exclude the addition of 211 for the treatment. Therefore, at this time, there are some differences between the compositional compositions of the steel blocks other than Zn, and the refining treatment can be further finely adjusted. • Step 3: Casting the molten steel of the second step to obtain the hot melt of the composition of the present invention by melting the molten steel which has passed through the first and second steps, and casting the third step of the present invention It is not limited to ordinary continuous casting or other special agglomeration methods. The toughness of the invention is improved by the addition of Zn; the majority of the bite is distributed, and the cold working tool steel which is greatly hindered by the weakening of the distribution of many carbides in the weaving is usually a less hot working tool with less carbide effect. The molten steel in the steel contains 〇'〇2% by mass. The step of adding Zn to the steel is combined with the above-mentioned first 5 weeks of tempering for the Zn step of P. For other purposes, if the goal is to make a new step to the steel block, the steel block is obtained. Moreover, the block method can also be used for the people, if in the organization. That is, the toughness described above in the group ' is sufficiently exhibited. 201250011 Therefore, the object of the present invention is defined as 钕 ς ς ^ 、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、、 Moreover, it can be applied to fineness in addition to JIS-specific steel grades. Hot work tools for μ, +, and micro cases. Ffi. U, ^ . Other than those specified in the above-mentioned hot work tool steel, can also be added as needed. The following is a manufacturing process of the present invention. # % 较佳, the preferred composition of the tool steel, the composition of the reason for the numerical limit. • C . 0 · 3 ~ below 〇 6 0/. Part C is solid-solubilized in the matrix to impart carbide formation while the tenth paralysis is from 4^ intensity' and one is c-invasive in the solid solution, when combined with alizarin. In addition, it has been changed; when f + it % 4 is added to the replacement of C with a large affinity, i (invasion, as a solution of 7' s (displacement atom), The effect of frictional resistance is only ",, A # ^. . It can also be expected that the addition of high-strength steel will lead to a decrease in knowledge. Therefore, it is better to use π A or ... for strength. ~ Below ..6%' is better than 〇55% • Si: 1.5% or less

Si係製鋼時的脫氧劑，同時為元素。為了得到茈笙4 m + 杈円素材的被削性之 A此專效果’亦可添加低加0.2%以上。掩 ^ · 、〇·2 /。，較佳添佳為1·5〇/0以下。等致肥粒鐵的生成，故較 • Μη : 1.5% 以下 Μη係具有接古 ’知阿泮火性，抑制肥粒度的淬火回火硬产成，得到適 ^ 效果。又，藉由作為非全眉八+ 1 的MnS存在，而淑a t r ~开隻屬介在物對於提咼被削性具有大@ 到此等效果，亦^ a ^ 负犬的效果。為了得了添加低於0.1%,但較佳為添加0.1% 201250011 以上。惟，若過多則會提高基體的黏度而使被削性降低 ’故較佳設為1 . 5 %以下。 • C r . 3.0 ~ 低於 6.0 % C r係提高淬火性，而且形成碳化物，具有強化基體或提高耐磨耗性之效果的元素。而且，係有助於提高回火軟化阻力及高溫強度之元素❶惟，過度的添加會導致淬火性或高溫強度的降低。因此，較佳為3.0〜低於6.〇〇/。。更佳為5.6 5 %以下。 * Mo及W係以單獨或複合，（m〇+1/2W): 3.5%以下The deoxidizer in the case of Si-based steel is also an element. In order to obtain the machinability of 茈笙4 m + 杈円 material, the special effect ' can also be added by 0.2% or more. Cover ^ · , 〇 · 2 /. Preferably, the preferred addition is less than 1·5〇/0. The formation of ferrite iron is equivalent to Μη: 1.5% or less. The Μη system has the effect of quenching and tempering, and suppressing the hardness of the granules. Moreover, by the presence of MnS as a non-full eyebrow + 1 +, the a t r ~ open is only a matter of the effect of having a large @ to this effect, and also a negative effect of the dog. In order to add less than 0.1%, it is preferable to add 0.1% 201250011 or more. However, if it is too large, the viscosity of the substrate is increased and the machinability is lowered. Therefore, it is preferably set to 1.5% or less. • C r . 3.0 ~ less than 6.0 % C r is an element that improves hardenability and forms carbides, which has the effect of strengthening the matrix or improving wear resistance. Moreover, it contributes to the improvement of the temper softening resistance and the high-temperature strength. Excessive addition causes a decrease in hardenability or high-temperature strength. Therefore, it is preferably 3.0 to less than 6.〇〇/. . More preferably 5.65% or less. * Mo and W are either alone or in combination, (m〇+1/2W): 3.5% or less

Mo及W係藉由回火而使微細碳化物析出或凝聚，而賦予強度，可單獨或複合地添加，用於提高軟化阻力。此時的添加量，由於W為Mo的約2倍之原子量，故可以（MO + 1/2W)的Mo當量一起規定（當然，可僅添加任一者，也可同時添加兩者）。而且’為了得到前述效果，能夠以（Mo + W2W)之值為低於丨.〇%添加，但較佳為添加 1.0%以亡。惟’由於若過多則會導致被削性或勒性的J 低，故較佳以（]^〇+1/2〜）之值為3.5%以下。 • V : 1.5 % 以下 |_叼償代性之效果。又，提高回火軟化阻力，抑制結晶粒化’有助於勒性的提高。為了得到此等效果，亦低於〇.5%’但較佳為添加〇.5%以上。惟，由於若過心會導致被削性或動性的降低，故較佳設為丨.5%以下。 -13- 201250011 • Ni : 1.5% 以下Mo and W are finely precipitated or aggregated by tempering to impart strength, and may be added singly or in combination to increase softening resistance. In the addition amount at this time, since W is about twice the atomic weight of Mo, the Mo equivalent of (MO + 1/2W) can be defined together (of course, either one may be added or both may be added at the same time). Further, in order to obtain the above effect, the value of (Mo + W2W) can be added below 丨.〇%, but it is preferable to add 1.0% to death. However, if it is too large, the J which is cut or the character is low, so the value of (]^〇+1/2~) is preferably 3.5% or less. • V: 1.5% or less |_ 叼代之。。 Further, increasing the temper softening resistance and suppressing crystal granulation' contribute to an improvement in the character. In order to obtain such effects, it is also less than 5%.5%', but it is preferably added by 5% or more. However, it is preferable to set it to 5% or less if the degree of cut or the kinetic property is lowered. -13- 201250011 • Ni : 1.5% or less

Ni係抑制肥粒鐵的生成之元素。又，與c、&、Μη 、,Mo、W等_起’賦予熱作卫具鋼優異的淬火性，即使當淬火時的冷卻速度緩慢時，亦形成麻田散鐵主體之組織’係防止韌性的降低用之有效的元素。再者，由於亦改善基體的本質勃性，於本發明中按照需要而添力”惟 ’若過多則提高基地的黏度而降低被削性。因此，即使添加時’較佳亦為⑽以下。再者’添加時，較佳為〇 1% 以上。 .Nb : 0.3%以下則係形成碳化物，具有強化基體或提高耐磨耗性之。又’由於提高回火軟化阻力’同時抑制結晶粒的且化’有助於動性的提高’在本發明中按照需要添加。惟’若過多則會導致被削性或韌性的降低。因此，即使添加時，亦較佳設為〇.3%以下。添加時，較佳為。㈣以上。 • Co : 5.0°/。以下Ni is an element that inhibits the formation of ferrite iron. Moreover, it is excellent in the hardenability of the hot work steel with c, &, Μη, Mo, W, etc., and even when the cooling rate at the time of quenching is slow, the structure of the main body of the granulated iron is prevented. The reduction of toughness is an effective element. Further, since the essence of the substrate is also improved, in the present invention, if necessary, if the amount is too large, the viscosity of the base is increased to reduce the machinability. Therefore, even when added, it is preferably (10) or less. Further, when it is added, it is preferably 〇1% or more. .Nb: 0.3% or less is formed into a carbide, has a reinforcing matrix or improves wear resistance, and 'because of improving temper softening resistance' while suppressing crystal grains In the present invention, it is added as needed. However, if it is too large, the machinability or toughness is lowered. Therefore, even when added, it is preferably set to 〇.3%. Hereinafter, when added, it is preferably (4) or more. • Co : 5.0 ° /.

Co係將本發明的熱作工具鋼當作工具使用中，而在其升溫時的表面上形成極緻密且密接性良好的保護氧化皮膜。此氧化皮膜係防止與對象材之間的金屬接觸制工具表面之溫度上升，同時帶來優異的耐磨耗性。因 :匕’於本發明中按照需要添加。惟’由於若過多則會使 “生降低，故添加日夺’亦較佳設為5 〇%以下。添較佳為〇. 3 %以上。 -14- 201250011 作為無可避免的雜質而有殘留在鋼中的可能性之主要凡素’係S、Cu、A卜Ca、Mg、〇(氧）、N(氮）等。為了有效地得到由於本發明之Zn添加的作用效果，此等元素較佳為儘可能地低。然而另一方面，為了得到介在物的形態控制或其它機械特性、製造效率的提高等的附加乍用效果，可多少含有及/或添加β此時，若為S盔0.01 〇/。In the Co system, the hot work tool steel of the present invention is used as a tool, and a protective oxide film having excellent density and good adhesion is formed on the surface at the time of temperature rise. This oxide film prevents metal contact between the target material and the temperature of the tool surface from rising, and at the same time, provides excellent wear resistance. Since 匕' is added as needed in the present invention. However, if too much is used, it will reduce the number of raw materials, so it is better to set it to 5 〇% or less. The addition is preferably 〇. 3 % or more. -14- 201250011 There is residue as an inevitable impurity. The main possibility in steel is 'S, Cu, A, Ca, Mg, 〇 (oxygen), N (nitrogen), etc. In order to effectively obtain the effect of the Zn addition of the present invention, these elements Preferably, it is as low as possible. On the other hand, in order to obtain an additional effect of controlling the morphology of the object, other mechanical properties, and improving the manufacturing efficiency, β may be contained and/or added. Helmet 0.01 〇 /.

Cu~ °·25% ' Al^ 0.025% > Ca^ 0.01% ^ Mg^ 0.01% > 〇$0·01%、Ν$〇〇3%之範圍，則可充分容許係為本發明的較佳管制上限。有關本發明的熱作工具鋼，作為為了充分發揮由於 η添加的韌性提尚效果之一形態，例如較佳為將鑄造後的鋼塊加工，在完成為鋼材之時施予均質化熱處理。或者’進一步使淬火回火硬度為5〇HRC以下較佳，更佳為 48HRC以下。 [實施例1 ] 藉由真空感應熔解爐，首先維持經調整成含有〇〇〇 5 質量％以上的P之熱作工具鋼的成分組成之熔鋼。此時的成分組成係以在進行以下的Zn添加（即Zn源的投入）後，成為目標的鋼塊之成分組成的方式來調整。而且，將鍍Zn鋼板用作為Zn源，於此熔鋼中添加Zn，進行鎮造，而製作7〜10kg的鋼塊。表！中顯示鑄造後的鋼塊之成分組成。Zn含量係藉由螢光χ射線分析來測定。本發明鋼係以在一般使用的熱作工具鋼JIS_SKD6l(p規格： ().〇30%以下）之成分組成中，添加滿足本發明的Zn/p比之Zn，為容許較多的p之含量者。再者，於全部的鋼塊 201250011 中，S、Cu、A1、Ca、Mg、Ο、N係無添加（惟，包含A1 在溶解步驟中作為脫氧劑添加的情況），係 S S 0.0 1 %、 CuS 0.25%、A1S 0.025%、CaS 0.01%、Mg S 0.01%、Ο S 0·01%、NS 0.0 3°/。。而且，於鑄造前添加有Zn的本發明鋼之P及Zn的含量，係可恰當地調整至指定的關係。相對於此，在上述真空感應熔解的初期添加 Zn時，Zn 係蒸發，於鑄造前的熔鋼中無法維持指定量的Zn。於上述的另一方面，為了說明本發明之Zn添加所致的效果，亦準備表1的比較鋼1〜6。此等比較鋼不添加 Zn(比較鋼6除外），僅增加SKD61的P之含量。而且， S、Cu、Al、Ca、Mg、Ο、N係無添加（惟，包含A1在溶解步驟中作為脫氧劑添加的情況），係 S S 0.0 1 %、Cu S 0.25%' Al^ 0.025%' Ca^ 0.01%' Mg^ 0.01%' 0.01% 、N S 0.0 3 %。表1 (質量％) 試料 C Si Μη Ρ Np Cr Mo 本發明鋼1 0.38 1.01 0.46 0.006 0.01 5.21 1.26 本發明鋼2 0.38 1.00 0.45 0.006 0.01 5.14 1.27 本發明鋼3 0.38 1.04 0.45 0.007 0.02 5.11 1.21 本發明鋼4 0,38 0.99 0.45 0.006 0.01 5.05 1.26 本發明鋼5 0.38 1.02 0.45 0.016 0.02 5.07 1.21 本發明鋼6 0.37 0.98 0.45 0.023 0.01 5.04 1.17 本發明鋼7 0.39 1.01 0.46 0.019 0.01 5.13 1.23 比較鋼1 0.38 1.03 0.44 0.007 0.01 5.19 1.24 比較鋼2 0.38 1.03 0.43 0.008 0.01 5.13 1.25 比較鋼3 0.38 1.02 0.44 0.016 0.01 5.25 1.23 比較鋼4 0.38 1.03 0.43 0.021 0.01 5.20 1.23 比較鋼5 0.39 1.02 0.43 0.039 <0.01 5.14 1.24 比較鋼6 0,38 0.97 0.43 0.039 0.01 5.21 1.28 201250011 試料 W*1 V Zn 抑※1 Co^1 Fe^2 Zn/P 本發明鋼1 <0.01 0.76 0.005 <0.01 <0.01 剩餘部分 0.83 本發明鋼2 <0.01 0.77 0.004 <0.01 <0.01 剩餘部分 0.67 本發明鋼3 <0.01 0.82 0.011 <0.01 <0.01 剩餘部分 1.57 本發明鋼4 <0.01 0.77 0.008 <0.01 <0.01 剩餘部分 1.33 本發明鋼5 <0.01 0.80 0.012 <0.01 <0.01 剩餘部分 0.75 本發明鋼6 <0.01 0.79 0.013 <0.01 <0.01 剩餘部分 0.57 本發明鋼7 <0.01 0.82 0.019 <0.01 <0.01 剩餘部分 1.00 比較鋼1 <0.01 0.82 <0.001 <0.01 <0.01 剩餘部分 <0.5 比較鋼2 <0.01 0.82 <0.001 <0.01 <0.01 剩餘部分 <0.5 比較鋼3 <0.01 0.82 <0.001 <0.01 <0.01 剩餘部分 <0.5 比較網4 <0.01 0.81 <0.001 <0.01 <0.01 剩餘部分 <0.5 比較鋼5 <0.01 0,82 <0.001 <0.01 <0.01 剩餘部分 <0.5 比較鋼6 <0.01 0.81 0.010 <0.01 <0.01 剩餘部分 0.26 無添加來2含有雜質對此等鋼塊，施予在1250°C的5小時之均質化熱處理後，以1150 °C熱作鍛造，而製作20mm厚度X60mm寬度X約500〜800mm長度的鋼材。而且，以86CTC退火處理k ’加工成下述評價用的夏比（Charpy)衝擊試驗片之尺寸，自103 0。(：進行油淬火處理，以各種的溫度來回火處理’而作為各種調質硬度的韌性之評價試料。 [試驗1 剛於本發明鋼1、3、5〜7及比較鋼i、3〜6，第i圖 :顯示各別的硬度在室溫的2 m m U缺口夏比衝擊試驗之、…果。夏比試驗片係依據ASTM E399-90的方向。於各別含有相同水準的p之本發明鋼〗、3及 ° 。與本發明叙I s » 較鋼1 ’ 4之組“比較鋼3 ’以及本發明鋼6、7及比較鋼、’、σ中’與未添加Zn的比較鋼1、3、4 士足本發明沾7 a J 4相比’以滿月的Zn/P比之方式添加有Zn的本發％ 5〜7係苜LU也姑々《刊鋼1、3、、夏匕衝擊值優異。而且’本發明鋼6儘管含有超 .201250011 過0.02%的高濃度之p，也藉由添加zn，而維持與p低於0.01 %的比較鋼1相同水準的韌性。比較鋼6雖然係為在含有同水準的P之比較鋼5中加有zn者，但未滿足本發明的Zn/P ’觀察不到韌性的提高。 [試驗2] 關於本發明鋼2、4〜7及比較鋼2〜6，第2圖中顯示調質為45HRC的硬度時之自室溫至4〇〇〇c之間的2mmv 缺口夏比衝擊試驗之結果。夏比試驗片係依據astm E399-90的T-L方向。於各別含有相同水準的p之本發明鋼2、4及比較鋼2，與本發明鋼5及比較鋼3，以及本發明鋼6、7及比較鋼4之組合中，與含有同水準的p 之比較鋼2〜4相比，以滿足本發明的Zn/p比之方式添加有Zn的本發明鋼2、4~7係在任一試驗溫度下皆夏比衝擊值優異，而且，雖然含有超過0.02%的高濃度之p，但藉由添加Zn，滿足本發明的Zn/p之本發明鋼6，係維持 -、P低於0.0 1 %的比較鋼2相同水準的韌性。 [實施例2 ] 藉由與實施例i記載之方法同樣的方法，製作具有 :二成分組成之鋼塊。本發明鋼A係在熱作工具鋼的刀、·且成中，添加滿足本發明的Zn/p比之Zn。而且， :了未添加Zn以外’比較鋼B係與本發明鋼成分組成者。再者，於兩者的鋼塊中，s、Cu、二的&Cu~ °·25% ' Al^ 0.025% > Ca^ 0.01% ^ Mg^ 0.01% > 〇$0·01%, Ν$〇〇3%, can be sufficiently tolerated as the preferred embodiment of the present invention The upper limit of control. In the hot work tool steel of the present invention, in order to sufficiently exhibit the effect of the toughness added by η, for example, it is preferable to process the steel block after casting, and to perform homogenization heat treatment when the steel material is completed. Or, the quenching and tempering hardness is preferably 5 〇 HRC or less, more preferably 48 HRC or less. [Example 1] A molten steel of a component composition of a hot work tool steel adjusted to contain P of 5% by mass or more was maintained by a vacuum induction melting furnace. The component composition at this time is adjusted so as to be a component composition of the target steel block after the following Zn addition (i.e., input of a Zn source) is performed. Further, a Zn-plated steel sheet was used as a Zn source, and Zn was added to the molten steel to carry out structuring to produce a steel block of 7 to 10 kg. table! The composition of the steel block after casting is shown. The Zn content was determined by fluorescence ray analysis. In the steel composition of the present invention, a Zn/p ratio Zn satisfying the present invention is added to a component composition of a hot work tool steel JIS_SKD6l (p specification: (). 〇 30% or less) which is generally used, and a large amount of p is allowed. Content. In addition, in all the steel blocks 201250011, S, Cu, A1, Ca, Mg, Ο, and N are not added (except that A1 is added as a deoxidizer in the dissolution step), and SS 0.0 1 %, CuS 0.25%, A1S 0.025%, CaS 0.01%, Mg S 0.01%, Ο S 0·01%, NS 0.0 3°/. . Further, the contents of P and Zn of the steel of the present invention to which Zn is added before casting can be appropriately adjusted to a predetermined relationship. On the other hand, when Zn is added in the initial stage of the vacuum induction melting, Zn is evaporated, and a predetermined amount of Zn cannot be maintained in the molten steel before casting. On the other hand, in the above, in order to explain the effects of the Zn addition of the present invention, Comparative Steels 1 to 6 of Table 1 were also prepared. These comparative steels do not contain Zn (except for Comparative Steel 6) and only increase the P content of SKD61. Further, S, Cu, Al, Ca, Mg, Ο, and N are not added (except that A1 is added as a deoxidizer in the dissolution step), and SS 0.0 1 %, Cu S 0.25% 'Al^ 0.025% ' Ca^ 0.01%' Mg^ 0.01%' 0.01%, NS 0.0 3 %. Table 1 (% by mass) Sample C Si Μη Ρ Np Cr Mo Steel of the invention 1 0.38 1.01 0.46 0.006 0.01 5.21 1.26 Steel 2 of the invention 0.38 1.00 0.45 0.006 0.01 5.14 1.27 Steel of the invention 3 0.38 1.04 0.45 0.007 0.02 5.11 1.21 Steel of the invention 4 0,38 0.99 0.45 0.006 0.01 5.05 1.26 Steel of the invention 5 0.38 1.02 0.45 0.016 0.02 5.07 1.21 Steel of the invention 6 0.37 0.98 0.45 0.023 0.01 5.04 1.17 Steel of the invention 7 0.39 1.01 0.46 0.019 0.01 5.13 1.23 Comparative steel 1 0.38 1.03 0.44 0.007 0.01 5.19 1.24 Comparative steel 2 0.38 1.03 0.43 0.008 0.01 5.13 1.25 Comparative steel 3 0.38 1.02 0.44 0.016 0.01 5.25 1.23 Comparative steel 4 0.38 1.03 0.43 0.021 0.01 5.20 1.23 Comparative steel 5 0.39 1.02 0.43 0.039 <0.01 5.14 1.24 Comparative steel 6 0, 38 0.97 0.43 0.039 0.01 5.21 1.28 201250011 Sample W*1 V Zn ※*1 Co^1 Fe^2 Zn/P Steel of the invention 1 <0.01 0.76 0.005 <0.01 <0.01 Remaining part 0.83 Steel 2 of the invention < 0.01 0.77 0.004 <0.01 <0.01 Remaining part 0.67 Steel of the invention 3 <0.01 0.82 0.011 <0.01 <0.01 Remaining part 1.57 Steel of the invention 4 <0.01 0.77 0.008 <0.01 <0.01 Remaining part 1.33 Steel of the invention 5 < 0.01 0.80 0.012 < 0.01 < 0.01 Remaining portion 0.75 Steel of the invention 6 < 0.01 0.79 0.013 < 0.01 < 0.01 Remaining portion 0.57 Steel of the invention 7 < 0.01 0.82 0.019 <0.01 <0.01 Remaining portion 1.00 Comparative steel 1 <0.01 0.82 < 0.001 < 0.01 < 0.01 Remaining portion <0.5 Comparative steel 2 < 0.01 0.82 < 0.001 < 0.01 < 0.01 Remaining <;0.5 Comparative steel 3 < 0.01 0.82 < 0.001 < 0.01 < 0.01 Remaining portion <0.5 Comparative net 4 < 0.01 0.81 < 0.001 < 0.01 < 0.01 Remaining portion < 0.5 Comparative steel 5 < 0.01 0,82 < 0.001 < 0.01 < 0.01 Remaining portion <0.5 Comparative steel 6 < 0.01 0.81 0.010 < 0.01 < 0.01 Remaining portion 0.26 No addition 2 impurities containing such steel blocks, given at 1250 After 5 hours of homogenization heat treatment at ° C, the steel was heat-forged at 1150 ° C to prepare a steel material having a thickness of 20 mm and a width X of about 500 to 800 mm. Further, the size of the Charpy impact test piece for the following evaluation was processed by the 86 CTC annealing treatment k ' from 103 0. (: Oil quenching treatment, round-fire treatment at various temperatures' as a test sample for toughness of various quenching and tempering hardness. [Test 1 Just in the steel of the present invention 1, 3, 5 to 7 and comparative steel i, 3 to 6 , i-fi: shows the 2 mm U-notch Charpy impact test for each hardness at room temperature. The Charpy test piece is based on the direction of ASTM E399-90. Inventive steels, 3 and °. Compared with the invention of the invention I s » compared steel 1 ' 4 group "compared steel 3 ' and the invention steel 6, 7 and comparative steel, ', σ medium' and not added Zn comparative steel 1, 3, 4, the foot of the present invention, 7 a J 4 compared to 'the full moon Zn / P ratio of the way to add Zn% of the hair 5 5 ~ 7 system 苜 LU also auntie ", steel, 1, 3, The Charpy impact value is excellent. Moreover, the Steel 6 of the present invention maintains the same level of toughness as Comparative Steel 1 having a p of less than 0.01% by adding zn despite the high concentration of p of 0.025% over 2020. Although the steel 6 is a zn added to the comparative steel 5 containing the same level P, the improvement of the toughness is not observed by the Zn/P' which does not satisfy the present invention. [Test 2] In the steels 2, 4 to 7 and comparative steels 2 to 6 of the present invention, the results of the 2 mmv notched Charpy impact test from room temperature to 4 〇〇〇c when the hardness is adjusted to 45 HRC is shown in Fig. 2. The test piece is based on the TL direction of astm E399-90. The steels 2, 4 and comparative steel 2 of the invention containing the same level of p, and the steel 5 and the comparative steel 3 of the invention, and the steel of the invention 6, 7 In the combination of the comparative steels 4, the steels 2, 4 to 7 of the present invention in which Zn is added in such a manner as to satisfy the Zn/p ratio of the present invention in comparison with the comparative steels 2 to 4 containing p of the same level are in any test. At the temperature, the Charpy impact value is excellent, and although the high concentration p is more than 0.02%, the steel of the present invention 6 satisfying the Zn/p of the present invention by adding Zn maintains - and P is less than 0.01 % of the comparative steel 2 has the same level of toughness. [Example 2] A steel block having a two-component composition was produced by the same method as the method described in Example i. The steel A of the present invention is a tool for hot work tool steel. Zn is added to meet the Zn/p ratio of the present invention, and the composition of the comparative steel B and the steel of the present invention is added except for the absence of Zn. Furthermore, the steel block of the two, s, Cu, II &

Mg、Ο、N係無添加（惟， — 劑添加），S<001。/ Γ 糸在浴解步驟中作為脫氧 )s=〇.〇1/o、Cu“25%、Alg〇〇25% 、Mg“.01%m〇1%、w%e - 0.0“ -18- 201250011 表2 試料 C λ Ίη Si Λ Mn P a Ni ~c；- Γ—Jtt%) 个贯納A 比較鋼B 0.38 U.Zo 0.30 0.60 0.56 0.007 U.OU 0.59 5.15 ____u〇 w^1 v Nb^1 Γλ※里 i ·5〇本發明鋼A Μ-知伽Ό <0.01 ^r\ m 0.65 π Δη 0.016 <0.01 Π1 <0.01 _Fe 效 2 乘 T20 ^U.U 1 <0.001 <U.UI 剩餘部分 5〇-5 浓1無添加效2含有雜質其次，對此等鋼塊，進行與實施例1同樣的熱作墙造及各種之熱處理，而製作已調質成各種硬度之夏比询^ 擊試驗片。而且，實施在實施例1所實施的夏比衝擊气驗1、2，評價各別的試料之韌性。 [試驗1] 關於本發明鋼A及比較鋼B，第3圖中顯示各別的硬度在室溫的2mmU缺口夏比衝擊試驗之結果。夏比試驗片係依據ASTM E399-90的L-S方向。此等鋼係藉由添加Ni，而當然韌性高者。而且，與未添加Zn的比較鋼B相比’以滿足本發明的Zn/P比之方式添加有Zn的本發明鋼A係夏比衝擊值優異。 [試驗2] 關於本發明鋼A及比較鋼b，第4圖中顯示調質為 45HRC的硬度時之自室溫至4〇(TC之間的2mmV缺口夏比衝擊試驗之結果。夏比試驗片係依據ASTM E399-9〇的L - S方向。於當然為勃性高的兩者之鋼中，更以滿足本發明的Zn/P比之方式添加有2^的本發明鋼A，係在任一试驗溫度下，與未添加2n的比較鋼b相比，皆夏比衝擊值優異。 .201250011 【圖發明試驗之本〇夏發明試驗之本〇夏【主式簡單說明】第1圖係於貫施例1中，將已調質成各種硬度之本鋼及比較鋼在室溫的2mmU缺口夏比衝擊值相對於片的硬度所繪製之圖。第2圖係於實施例1中，將已調質成45HRC的硬度發明鋼及比較鋼之自室溫至400。(：之間的2mmV缺比衝擊值相對於試驗溫度所繪製之圖。第3圖係於實施例2中，將已調質成各種硬度之本鋼及比較鋼在室溫的2mmU缺口夏比衝擊值相對於片的硬度所繪製之圖。第4圖係於實施例2中，將已調質成45HRC的硬度土明鋼及比較鋼之自室溫至400°C之間的2mmV缺比衝擊值相對於試驗溫度所繪製之圖。要元件符號說明】益〇 -20-Mg, Ο, N are not added (only, added), S < 001. / Γ 作为 as a deoxidation in the bathing step) s=〇.〇1/o, Cu “25%, Alg〇〇25%, Mg “.01%m〇1%, w%e - 0.0” -18- 201250011 Table 2 Samples C λ Ίη Si Λ Mn P a Ni ~c;- Γ—Jtt%) 贯 A A Compare steel B 0.38 U.Zo 0.30 0.60 0.56 0.007 U.OU 0.59 5.15 ____u〇w^1 v Nb^ 1 Γλ※里i ·5〇The steel of the invention A Μ-zhijia Ό <0.01 ^r\ m 0.65 π Δη 0.016 <0.01 Π1 <0.01 _Fe effect 2 times T20 ^UU 1 <0.001 < U. The remaining part of the UI is 5〇-5, the concentration is 1, the additive effect is 2, and the impurities are second. For the steel blocks, the same hot work as in the first embodiment and various heat treatments are carried out, and the summer heat ratio of the various hardnesses is prepared. The test piece was inquired, and the Charpy impact test 1 and 2 carried out in Example 1 were carried out to evaluate the toughness of each sample. [Test 1] Steel A and Comparative Steel B of the present invention, Fig. 3 The results show the results of the 2mmU notched Charpy impact test for each hardness at room temperature. The Charpy test piece is based on the LS direction of ASTM E399-90. These steels are of course tough by the addition of Ni. With or without added Zn Compared with steel B, the steel A of the present invention in which Zn is added in such a manner as to satisfy the Zn/P ratio of the present invention is excellent in Charpy impact value. [Test 2] Regarding the steel A of the present invention and the comparative steel b, in Fig. 4 The results of the 2 mmV notched Charpy impact test between room temperature and 4 〇 (Temperature test results are shown in the L-S direction according to ASTM E399-9〇). In the high steel of the two, the steel A of the present invention is further added to meet the Zn/P ratio of the present invention, at any test temperature, compared with the comparative steel b to which no 2n is added. The Charpy impact value is excellent. .201250011 [The invention of the test of the summer of the invention test of the summer of the summer [main type of simple description] The first picture is in the first example, the fine steel has been tempered into various hardness and Comparing the 2mmU notched Charpy impact value of steel at room temperature with respect to the hardness of the sheet. Fig. 2 is a diagram showing the hardness of the inventive steel and the comparative steel from room temperature to 400 in the first embodiment. (: between 2 mmV and the specific impact value plotted against the test temperature. Figure 3 is in Example 2, This quenching into a variety of steel and the comparative steel hardness plotted in FIG impact value of hardness at room temperature relative to the notch Charpy 2mmU sheet. Fig. 4 is a graph in which the 2 mm V specific impact value between room temperature and 400 ° C of the hardness of 45 HRC and the comparative steel was adjusted to the test temperature in Example 2. Element symbol description] 益〇 -20-

Claims

201250011 VII. Patent application scope: 1. A hot work tool steel with excellent toughness, containing C: 0.3 ~ less than 0 · 6 %, S i : 1.5 % or less, Mn : 1.5 % or less, in mass % Cr: 3.0 to less than 6.0% of hot work tool steel, characterized by: Ζη: more than 0.0025 to 0.025%, Ρ: 0.005% or more, and Ζη/Ρ: more than 0.5. 2 • The hot work tool steel with excellent toughness as in the first application of the patent scope is in mass%, and the Mo and W systems are either alone or in combination, containing (MO+1/2W): 3.5% or less. 3. The hot work tool steel having excellent toughness as in the first or second patent application is in a mass%, and contains V: 1.5% or less. 4. For hot work tool steels having excellent edge resistance according to item 1 of the patent application, in terms of mass%, C: 0.3 to less than 0.6%, S i : 1.5% or less, Mn: 1.5% or less, Ni : 1.5% or less (including 0%), Cr: 3.0 to less than 6.0%, Mo and W alone or in combination, (MO + 1/2W): 3.5% or less, V: 1.5% or less, Nb: 0.3% or less (including 0%), Co: 5.0% or less (including 0%), Zn: more than 0.0025 to 0.025%, P: 0.005% or more, and Ζη/Ρ: more than 0.5, and contains the remaining part of Fe and inevitable Impurities. -2 1- 201250011 5·The hot work tool with excellent toughness as in the first or fourth patent application area is 〇〇 1 〇/0 or more in terms of mass 〇/〇. A method for producing a hot work tool steel excellent in physical properties, comprising: a first step of obtaining a molten steel having a composition of hot work tool steel containing 0.005 mass% or more, and a hot work tool a second step of adding Ζη to the molten steel of the composition of steel, and a third step of casting a molten steel obtained by adding ζη to the steel, wherein the second step is to make the third step after casting The composition of the steel block is 方式η: a method of containing Ζη: more than 0.0025 to 0.025 mass%, Ρ0.005 berry% or more, and Ζη/ρ: a hot work tool steel exceeding 〇5, and adding Ζη. 7. If the patented rib is applied, (5) the manufacturing method of the hot work tool steel with excellent toughness of item 6, wherein the composition of the steel block after casting in the third step of the third step is the mass % Α °τ ' C : 〇. 3 ~ less than 〇. 6 %, S i : 1.5 % or less, Μη: 1.50/〇 with τ ^ lower, Cr: 3.0 to less than 6.0% hot work tool steel. 8. For the manufacturing method of hot work tool steel with excellent toughness as claimed in Item 7 of the patent, the composition of the steel block after casting in the third step of the stocking is in mass % nt ' Mo and w alone or Composite, containing (Mo + l / 2W): 3 5V p, Λ, , 5 / °U under the hot work tool steel. 9. If the toughness of the hot work tool steel No. 7 or 8 of the patent application plan is applied, the composition of the steel block after casting is the mass of 0. ® / () meter 'V: 1.5% or less of hot work tool steel-22-.201250011 10. The method of manufacturing the hot work tool steel with excellent toughness as claimed in item 6 of the patent application, wherein the casting of the third step The composition of the subsequent steel block is in mass%, C: 0.3 to less than 0.6%, S i : 1.5% or less, Μ η : 1 · 5 % or less, Ni: 1.5% or less (including 0%), Cr : 3.0~ less than 6.0%, Mo and W are separate or composite, (MO+1/2W): 3.5% or less, V: 1 · 5 % or less, Nb : 0.3% or less (including 0%), Co : 5.0 % or less (including 0%), Zn: more than 0.0025 to 0.025%, P: 0.005% or more, and Zn/P: more than 0.5, and contains the remaining part of Fe and inevitable impurities as hot tool steel. 11. The method for producing a hot work tool steel having excellent toughness as claimed in claim 6 or 10, wherein the composition of the molten steel obtained in the first step is % by mass, and contains P: 0.01% or more. The composition of the steel block after casting in the third step is, in mass%, P: 0.01% or more. -twenty three-