TWI358458B - Cold work tool steel - Google Patents

Description

1358458 九、發明說明： 一、【發明所屬之技術領域】 本發明係關於冷作工具鋼，尤有關於適合各種不同冷模之冷 作工具鋼，例如冷锻衝孔模、高抗拉強度鋼板之成形模、彎曲模、 冷鍛模、型緞模、螺紋滾（製）模、衝頭構件、開縫刀具、引線 框T料模、量規、深引伸衝頭、彎曲模衝頭、剪切刀、不銹鋼彎 曲模、引伸模、冷壓用塑性加工工具、齒輪用衝頭、突輪零件、 下料衝壓模、級進式下料模、泥砂饋料機之封板、螺紋構件、混 凝土噴塗機之旋轉盤、1C封模、及要求高尺寸精度之精密衝壓模， • 以及經表面處理（例如CVD處理、PVD處理或TD處理）後所佬 用之上述冷模。1358458 IX. Description of the invention: 1. Technical field to which the invention belongs. The present invention relates to cold-work tool steel, and particularly to cold-work tool steels suitable for various cold molds, such as cold forging punching dies and high tensile strength steel sheets. Forming die, bending die, cold forging die, type satin die, thread rolling die, punch component, slitting tool, lead frame T die, gauge, deep extension punch, bending die punch, shear Cutting knives, stainless steel bending dies, extension dies, plastic working tools for cold pressing, punches for gears, burr parts, blanking dies, progressive feeding dies, sealing plates for mud sand feeders, threaded members, concrete Rotating discs for sprayers, 1C seals, precision stamping dies requiring high dimensional accuracy, and the above-mentioned cold dies used after surface treatment (eg CVD, PVD or TD).

二、【先前技術】 藉由結晶或沈澱來分散大量高硬度碳化物，可增強以JIS鋼 材SKD 11表示之冷肛具鋼之财雜性，並可使之祕要求耐磨 耗性或耐擦黏性之各種不關途（例如冷鍛衝孔模、冷锻模等） 上；然而’習知冷作工具鋼仍有下列問題：⑴勃性不足' 成條件硬化等賴顯具硬度；及⑶線_放電加工之斷裂 性。 因此’吾人傳統上提出各種不同之方法來解決這些 如引證專利1揭露-種冷作卫具鋼，包含C:G 7^ 175加。 0.5 至 3.0 wt%、Mn: 0J 至 2.0 斯％、Cr: 5 〇 至 u 〇 初％、m ㈡0二°1、Ζΐ1 ΐ 5.°—、及剩餘部分Fe與雜質，其係於45 (：或更_度下回火，引證專利丨中亦說明了吾人 主 。共熔碳?物最少化來增強祕，並可在織各組成時，藉 $ C $更=度下敎以提升二次硬化硬度（攸 曰 hardness)來大幅提升工具壽命及放電加工性。 引證專利2揭露-種具有—預定組成之冷作卫且並 100哗或更小之碳化物黏聚部分之黏聚尺寸；引證^利2 5 之將黏聚尺寸設定在100 μιη或更小而加 1中揭露—種具有一預定組成之高硬度冷作工具鋼， i 1 0 > LTr 〇Ml C' °·063 Cr + °·033 M〇 · °*232 V) ^ °·7 3亦却明j,·、ΓΜ〇當量+1.9V當量）為3.0至6.0;引證專利 在=lb r囹为碳化物及黏聚碳化物之形成可藉由將α值及p值設定 在每些1_改善與硬表面層間之黏附性。 又疋 1中專，4揭露—種具有一預定組成之高硬度冷作工具鋼， 栌Anm /〇之殘留沃斯田鐵（retained austenite)係以平均粒 =二至殘 且細再證專利5揭露—種具有—預定組成之高硬度冷作工 ^性.引级少、C含量時可加人高速切削元素’以改善加 止因放電之以賊聽力可糊高邮絲移除，以防 [引，專利1]日本專利申請案公開號859_179762 [引，專利2]日本專利申請案公開號2〇〇2_12952 [引，專利3]日本專利申請案公開號2〇〇〇_〇73 i42 [引證專利4]日本專利申請案公開號2〇〇4_〇3592〇 [引證專利5]日本專利申請案公開號2〇〇〇_355737 於握具^及小產品編號之模具特別要求優異可加工性更甚 具鋼，HRC 6〇者可在保有以任何加工方法 削、放電加工、以及線切割放電加工）之加 二2 -般模具相同之硬度。 Μ乃具有與 然而，以SKD 11來表示之習知冷作工具鋼， J下仍巧加X性極差_題，因為結晶碳化物係大量竑2 引發線斷裂。 才、、、口曰曰衩化物常 吾^亦已知其巾結晶碳錄量被減少至可改善其可加工性之 =淬;時在材料中所產生之應力便無法去 之材料施行放電加工或線切割放電加工時，殘餘應力可 月b失去平衡而導致材料之斷裂或毀損。 、…、 量較s在κ^,1戶ί揭露之冷作工具鋼中，因其結晶碳化物減少 2 ^夕，且組成會受到調整，如此可確保HRC 60或更大 硬又’且可加工性可提升至某些程度 =ί f ^之改良仍嫌不== 利至5並未揭路在保有高硬度時可改良可加工性之具體裝置。 三、【發明内容】 值，發明之目的於是在於提供回火後具有HRC 60或更大硬度 之優異可加工性之冷作工具鋼。 根據本發明之冷作工具鋼包含：〇4$κ值^2 6 (κ值=(> jwt%) · 6.8 C (wt%)) ; 15·5紅值迎 〇 (L 值=〇_(感）+ 15 5 c (wt〇/〇)) ； 0.60 wt〇/〇<Si^2.0 wt〇/〇 ； 0.10 wt%^Mn^ 1.0 wt% ； 0.03 wt% < S ^ 0.2 wt% ； 1.25 wt% < Mo + 0.5 W < 3.0 wt% ； 0.05 wt% ^ VSl.Ow^/o，以，剩餘部分Fe與無可避免之雜質，其中藉由淬火 後在450 C或更高溫度下回火所得之最大硬度為hrc 61或更大 值。 根據本發明之冷作工具鋼，因尺值係設定於一預定範圍，故 士 HRC 6^ $更大值之高溫回火後可得一最大硬度；因[值係固 定於-預定範®，故可改良加工性，且可抑制在線切割放電加工 上線的斷裂；再者，因除了 S之外另加入06wt%或更多的以，故 可獲知4同於或優於習知高速切削鋼材之加工性。 四、【實施方式】 1358458 兹將詳細·本發明之較佳實施例。本發明之冷作工且鋼包 含下列元素、剩餘料Fe與無可避免之雜質；待添加之元素種類、 組成範圍及其限制理由如下所示。 (1) 0.4^Κ 值S2.6 (K 值=Cr (wt%) - 6.8 C (wt%)) κ值表示在適當淬火溫度下基質中之殘餘Cr含量。當κ值小 於0.4或大於2.6時’即降低了所形成之有助於回火時二次硬化之 =物量，以致於45(TC或更高溫度的回火不易獲得硬度為脈 或更大值之鋼材，又κ值最好為大於或等於045及小於或等於 2.5，若為大於或等於0.6及小於或等於2 4則更佳。 (2) 15.5f L 值 $21 .〇 (L 值=Cr (wt%) + 15.5 C (wt0/〇))2. [Prior Art] By dispersing a large amount of high-hardness carbide by crystallization or precipitation, the financial property of cold anal steel expressed by JIS steel SKD 11 can be enhanced, and the wear resistance or rub resistance can be claimed. Various types of viscous are not related (such as cold forging punching die, cold forging die, etc.); however, the conventional cold working tool steel still has the following problems: (1) insufficient boring property, conditional hardening, etc.; (3) Breakage of wire_discharge machining. Therefore, we have traditionally proposed various methods to solve these problems, as disclosed in the cited patent 1 - a kind of cold-worked steel, including C: G 7^ 175 plus. 0.5 to 3.0 wt%, Mn: 0J to 2.0 s%, Cr: 5 〇 to u 〇 initial %, m (two) 0 °1, Ζΐ1 ΐ 5.°—, and the remaining Fe and impurities, which are at 45 (: Or tempering under _ degrees, the patent cited in the 丨 说明 说明 亦 亦 亦 亦 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 Hardening hardness (大幅hardness) to greatly improve tool life and electrical discharge processability. Citation Patent 2 discloses a cohesive size of a carbide-bonded portion having a predetermined composition of cold work and 100 哗 or less; ^利2 5 The cohesive size is set at 100 μηη or less and added 1 to reveal a high hardness cold work tool steel with a predetermined composition, i 1 0 > LTr 〇Ml C' °·063 Cr + °·033 M〇· °*232 V) ^ °·7 3 also shows that j, ·, ΓΜ〇 equivalent +1.9V equivalent) is 3.0 to 6.0; the cited patent is carbide and cohesive carbonization at =lb r囹The formation of the substance can be achieved by setting the alpha value and the p value between each of the 1_-improved adhesion to the hard surface layer. Also 中1 secondary school, 4 reveals a kind of high-hardness cold-work tool steel with a predetermined composition, 栌Anm / 〇 residue remaining austenite (average grain = two to the residual and fine re-certification patent 5 Exposure - a kind of high hardness cold work with a predetermined composition. Less lead, C content can be added to the high-speed cutting element 'to improve the stop-and-discharge discharge of the thief hearing can be high-definition wire to prevent [ Japanese Patent Application Publication No. 859-179762, Japanese Patent Application Publication No. 2 〇〇 2 _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ Japanese Patent Application Publication No. 2〇〇4_〇3592〇 [cited patent 5] Japanese Patent Application Publication No. 2 〇〇〇 355737 Specially required for excellent moldability in molds of grips and small product numbers Even more steel, HRC 6 can be used in any processing method, cutting, electrical discharge machining, and wire-cut electrical discharge machining) plus the same hardness of the same mold. However, the conventional cold work tool steel, represented by SKD 11, is still very difficult to add X, because the crystalline carbide is a large amount of 竑2 to cause wire breakage.才,,和口曰曰衩化常吾^ It is also known that the crystal carbon footprint of the towel is reduced to improve the processability = quenching; Or during wire-cut electrical discharge machining, the residual stress may be out of balance at month b, resulting in fracture or damage of the material. , ..., the amount of s in the κ ^, 1 household ί exposed cold work tool steel, because its crystalline carbide is reduced by 2 夕, and the composition will be adjusted, thus ensuring HRC 60 or more hard and 'can The processability can be improved to some extent = ί f ^ The improvement is still not == 5 is not disclosed in the specific device that can improve the processability when maintaining high hardness. 3. SUMMARY OF THE INVENTION The value of the invention is to provide a cold-work tool steel having excellent workability of HRC 60 or more after tempering. The cold work tool steel according to the present invention comprises: 〇4$κ value ^2 6 (κ value = (> jwt%) · 6.8 C (wt%)); 15·5 red value 〇 (L value = 〇 _ (Sense) + 15 5 c (wt〇/〇)); 0.60 wt〇/〇<Si^2.0 wt〇/〇; 0.10 wt%^Mn^ 1.0 wt% ; 0.03 wt% < S ^ 0.2 wt% 1.25 wt% < Mo + 0.5 W < 3.0 wt% ; 0.05 wt% ^ VSl.Ow^/o, to the remaining part of Fe and inevitable impurities, which are quenched at 450 C or higher The maximum hardness obtained by tempering at a temperature is hrc 61 or more. According to the cold working tool steel of the present invention, since the rule value is set to a predetermined range, the maximum hardness can be obtained after the high temperature tempering of the greater value of the HRC 6^ $; since the value is fixed at - the predetermined range, Therefore, the workability can be improved, and the breakage of the on-line cutting electric discharge machining can be suppressed. Further, since 06 wt% or more is added in addition to S, it is known that 4 is the same as or better than the conventional high-speed cutting steel. Processability. Fourth Embodiment [Embodiment] 1358458 A preferred embodiment of the present invention will be described in detail. The cold work of the present invention and the steel contains the following elements, the remaining Fe and the inevitable impurities; the types of elements to be added, the composition range and the reasons for the limitation are as follows. (1) 0.4^Κ Value S2.6 (K value = Cr (wt%) - 6.8 C (wt%)) The κ value indicates the residual Cr content in the matrix at a suitable quenching temperature. When the κ value is less than 0.4 or greater than 2.6, the amount of secondary hardening that contributes to tempering is reduced, so that 45 (TC or higher temperature tempering is difficult to obtain hardness as a pulse or greater). For the steel, the κ value is preferably greater than or equal to 045 and less than or equal to 2.5, and more preferably greater than or equal to 0.6 and less than or equal to 2 4. (2) 15.5f L value of $21. 〇 (L value = Cr (wt%) + 15.5 C (wt0/〇))

Lj顯示㈣巾結晶碳化物之含量；L值愈大，結晶碳化物之 =愈夕。當L值小於15.5時，不僅因為結晶碳化物不易形成， 因在適當較溫度下之歸組成改變，故纽得到必要硬 ^，备值超過A 〇時’即表示結晶碳化物含量過度地增加，如 此則破壞了加工性、放電加工性以餘性。然而 ’因在淬火時若完全無結晶碳化物將使: ^化，夾雜各種不同之顆粒尺寸；L值大於或#於15· 8且小 4於20. 8更好，最好為大於或等於16· 〇且小於或等於2〇 5。一 結曰曰曰碳」匕物意謂圓形對應直徑（circle肅〇 f )超過約10哗之碳化物，主要由Μ心來代表（M代表§ r，〇等），15.5至21. 0之L值即對應於〇. 2〇至4. 〇 wt%之έ士曰 碳化物。 wc/〇^^0 a0 (3) 0.60 wt%<Si^2.0 wt% 發明ΐ 為Λ減元素’故其通常包含於鋼材内。在本 it僅ΐΐ生於退火後之低硬度（約腦95)狀態，亦發ΐί 回火後之两硬度狀態⑽C01或更添加 於 改良高溫回火硬度。 助於 為獲得此—效果，必須添加超過0.6 wt%含4之Si，即使再過 8 1358458 量添加Si ’但效果已達飽和，因此，Si含量最好設定於2.0 wt%或 更低’又石夕含量為0.65 wt%或更大以及1.8 wt%或更小較佳，若為 〇*7wt%或更大以及1 5wt%或更小則更佳。 (4) 0.10 wt% ^ Μη ^ 1.0 wt% Μη具有增加可硬化性以提升硬度與強度之效用，其與高速切 削元素S反應，藉此形成包合物(inciusi〇n)以有效地改善切削性 質。為獲得此一效果，所需之Μη添加量為0.10 wt%或更多；當 過量添加Μη時’即破壞了熱加工性，因此，Μη含量最好為1 .〇 wt% 或更低。 (5) 0.03 wt% ^ S ^ 0.2 wt% S為一高速切削元素，其會與Μη鍵結以形成包合物而改良加 工性’因添加S可獲得之改良加工性不僅只發生於退火後之低硬 度（約HRB 95)狀態’亦發生於淬火或回火後之高硬度狀態（HRC 61或更大）。 為獲得此一效果’必須添加0.03 wt%或更多含量之S，當過量 添加S時’材料區塊中之查比衝擊（Charpy impact)值將大幅衰 減’因此’ Si含量最好設定於〇.2 wt%或更低。 (6) 1.25 wt% <Mo + 0.5 W< 3.0 wt%Lj shows the content of (4) the crystal carbide of the towel; the larger the L value, the more the crystalline carbide = the eve. When the L value is less than 15.5, not only is the formation of crystalline carbides difficult to form, but the composition of the composition is changed at a suitable temperature, so that the necessary hardness is obtained, and when the value exceeds A 〇, the content of the crystalline carbide is excessively increased. This destroys the workability and the electrical discharge processability. However, if there is no crystallized carbide at the time of quenching, it will be: ^, mixed with various particle sizes; L value is greater than or #15 and 8 is less than 20. 8 is better, preferably greater than or equal to 16· 〇 and less than or equal to 2〇5. A crucible carbon" means that the circular corresponding diameter (circle is f) exceeds about 10 碳 of carbide, mainly represented by the heart (M stands for § r, 〇, etc.), 15.5 to 21. 0 The L value corresponds to έ. 2〇 to 4. 〇wt% of the 曰士曰 carbide. Wc / 〇 ^ ^ 0 a0 (3) 0.60 wt% < Si ^ 2.0 wt% Invention ΐ is a reduced element ', so it is usually contained in steel. In this case, it is only found in the low hardness (about 95) state after annealing, and also in the two hardness states (10) C01 after tempering or added to the modified high temperature tempering hardness. In order to obtain this effect, it is necessary to add more than 0.6 wt% of Si containing 4, even if Si 1 is added in an amount of 8 1358458, the effect is saturated, so the Si content is preferably set at 2.0 wt% or lower. The Shi Xi content is preferably 0.65 wt% or more and 1.8 wt% or less, more preferably 〇*7 wt% or more and 15 wt% or less. (4) 0.10 wt% ^ Μη ^ 1.0 wt% Μη has the effect of increasing hardenability to improve hardness and strength, and reacts with high-speed cutting element S, thereby forming an inclusion compound (inciusi〇n) to effectively improve cutting. nature. In order to obtain this effect, the amount of Μη added is 0.10 wt% or more; when the Μη is excessively added, the hot workability is deteriorated, and therefore, the Μη content is preferably 1. 〇 wt% or less. (5) 0.03 wt% ^ S ^ 0.2 wt% S is a high-speed cutting element that bonds with Μη to form an inclusion compound to improve processability. The improved processability obtained by adding S not only occurs after annealing. The low hardness (about HRB 95) state also occurs in the high hardness state after quenching or tempering (HRC 61 or greater). In order to obtain this effect, it is necessary to add 0.03 wt% or more of S. When S is excessively added, the Charpy impact value in the material block will be greatly attenuated. Therefore, the Si content is preferably set at 〇. .2 wt% or lower. (6) 1.25 wt% <Mo + 0.5 W< 3.0 wt%

Mo及W係形成碳化物，以增加在45〇。(：或更高溫度下進行回 火^二次硬化量。雖然Mo及w具有相同效果，但為具有與 相等之效果，需要雙倍W量’故Mo及W含量係由Mo + 0.5 W 所述之Mo當量來調整。 在淬火及回火後，為獲得HRC 61或更大之硬度，Mo當量須 大於1.25 wt% ;然而，當Mo當量過大時，熱加工性、韌性、及 加工性即顯惡化’因此，Mo當量最好小於3.〇 wt〇/〇。 (7) 0.05 wt%^V^ 1.0 wt% V係开>成穩疋％化物以有效地防止顆粒粗化，其亦有助於藉 由形成碳化物來改良耐磨耗性及硬度。為獲得這此效果，須乂 加⑽爾更多含量之V，當V含量過高時，因碳f匕物以 1358458 =令加工性及熱加雜降低，因此’ v含量最好設定於丨〇加％ 或更低。 除了上述元素外，本發明之冷作工具鋼可更包含下述之一或 更多兀素，各兀素之組成範圍及限制理由將說明如下。 (8) 0.005 wt%^Se^〇.l〇 wt% (9) 0.005 wt%$Te$ 0.10 wt% (10) 0.0002 wt%^Ca^O.〇i〇 wt〇/〇 (11) 0.005 wt%^Pb^〇.i〇 wto/o (12) 0.005 wt%^Bi^〇.i〇 wt% 吾人可添加Se，Te，Ca，Pb及/或Bi以提升加工性，加入這些 疋素且添加Si並不會抑制加工性上之改良。 f Mn_硫化物中，Se及Te可作為s之替代元素；Q 由 J成氧化物或溶解於Μη·硫化物中，以於加工時在切削工且^ 提升加卫性；χ ’加卫所產生之熱將令低^點材 力熔融，以期於切削工具與切角間產生潤滑效果，來 為獲得此種效果，上述元素之添加量必須大於或等於其下限 ，，因過度添加這些元素將破壞鋼材之機械特性，故盆力^ 好設定在小於或等於上述上限。 ’、、、取 (13) 0.01 wt%^Cu^2.0wt% (14) 0.01 wt%^Ni^2.0 wt% (15) 0.20 wt%^Co^ 1.0 wt% (16) 0.0003 wt%^B ^0.010 wt% # CULNi，C〇及B係溶解於基質中以有效地提升可硬化性；Ni 二^有藉由減少衝擊轉移（impacttransiti〇n)溫度以增加 鋼提升以避免破壞鍛接性之效果。在冷模中，依高抗拉強i ώ或工作條件’常有因加工發熱（working-heating )而佶模且、、田 情形。C。具有藉㈣-溫度提升以增進高ϊϊ度= 尤棋具發生永久變職效果。為獲得這些效果，這些元素的添 1358458 加^最好設定於大於或等於上述下限值；因過度添加這些元素 破壞鋼材之機械特性，故其添加量最好設定在小於或等於上述上 限值。 、 (17) 0.001 wt%^P^0.030 wt% (18) 0.0050 wt%^N^0.050 wt% (19) 0.001 wt%^A1^0.10 wt% (20) 0.0002 wt%^0^0.010 wt% P，N，0係無可避免地包含於鋼材中，p隔離於顆粒邊界中，〇 形成氧化物，且N形成氮化物。在鋼材中，A1與〇或N反應以 ❿形成氧化物或氮化物，這些元素可藉由減少其添加量來提升韌 性。為獲得此一效果，這些元素的添加量最好設定於小於或等於 上述上限值；最好P佔0.020加％或更少，n佔0.030糾％或更少， A1佔0.050 wt%或更少’ 〇佔0.050 wt0/〇或更少。 ’ A1之氧化物或氮化物有助於防止顆粒粗化，是故若這些元素 ' 含f過度稀少，顆粒反之即變粗而破壞鋼材韌性。為減少^於需 -要量的這些元素含量，將會增加製造成本；又，當這些元素達到 或小於某些固定值時，提升韌性的效果亦達飽和，因此，這些元 素的含量最好設定在大於或等於上述下限值。 (21) 0.010 wt%^Nb^0.10 wt% ® (22) 0.005 wt%^Ta^〇.l〇 wt% (23) 0.005 wt%^Ti^〇.l〇 wt% (24) 0.005 wt%^Zr^0.10 wt% (25) 0.005 wt%^ Mg ^0.10 wt% (26) 0.005 wt%^ REM^0.10 wt%Mo and W systems form carbides to increase at 45 Å. (: or tempering at a higher temperature ^ secondary hardening amount. Although Mo and w have the same effect, in order to have equal effect, double W amount is required', so Mo and W content are from Mo + 0.5 W The Mo equivalent is adjusted as described. After quenching and tempering, in order to obtain a hardness of HRC 61 or more, the Mo equivalent must be greater than 1.25 wt%; however, when the Mo equivalent is too large, hot workability, toughness, and workability are It is markedly deteriorated. Therefore, the Mo equivalent is preferably less than 3. 〇wt〇/〇. (7) 0.05 wt%^V^ 1.0 wt% V is opened and stabilized to effectively prevent coarsening of the particles. It helps to improve the wear resistance and hardness by forming carbides. In order to obtain this effect, it is necessary to add more than 10% of V. When the V content is too high, the carbon f is 1358458 = The processability and the thermal addition are reduced, so the 'v content is preferably set to 5% or less. In addition to the above elements, the cold-work tool steel of the present invention may further comprise one or more of the following, each The composition range and limitation reasons of 兀素 will be explained as follows. (8) 0.005 wt%^Se^〇.l〇wt% (9) 0.005 wt%$Te$ 0.10 wt% (10) 0.0002 wt% ^Ca^O.〇i〇wt〇/〇(11) 0.005 wt%^Pb^〇.i〇wto/o (12) 0.005 wt%^Bi^〇.i〇wt% We can add Se,Te, Ca, Pb and/or Bi improve workability, and adding these alizanes and adding Si does not inhibit the improvement of workability. f Mn_sulphide, Se and Te can be used as substitutes for s; Q is formed by J Oxide or dissolved in Μη· sulphide, so as to improve the edging during the machining process; χ 'The heat generated by the Guardian will melt the low point material, in order to produce lubrication between the cutting tool and the chamfer The effect is that, in order to obtain such an effect, the addition amount of the above elements must be greater than or equal to the lower limit, and excessive addition of these elements will destroy the mechanical properties of the steel, so the pot force is preferably set to be less than or equal to the above upper limit. Take (13) 0.01 wt%^Cu^2.0wt% (14) 0.01 wt%^Ni^2.0 wt% (15) 0.20 wt%^Co^ 1.0 wt% (16) 0.0003 wt%^B ^0.010 wt% # CULNi, C〇 and B are dissolved in the matrix to effectively enhance the hardenability; Ni 2 has the effect of increasing the steel lift by reducing the impact transfer temperature to avoid breaking the forge. In the cold mold, depending on the high tensile strength i ώ or working conditions, 'there is often a mold due to working-heating, and the field. C. With (four) - temperature increase to improve high twist = especially chess A permanent change effect occurs. In order to obtain these effects, the addition of 1358458 to these elements is preferably set to be greater than or equal to the above lower limit; since excessive addition of these elements destroys the mechanical properties of the steel, the addition amount is preferably set to be less than or equal to the above upper limit. . (17) 0.001 wt%^P^0.030 wt% (18) 0.0050 wt%^N^0.050 wt% (19) 0.001 wt%^A1^0.10 wt% (20) 0.0002 wt%^0^0.010 wt% P The N, 0 system is inevitably contained in the steel, p is sequestered in the grain boundary, niobium forms an oxide, and N forms a nitride. In steel, A1 reacts with niobium or N to form oxides or nitrides, which can increase toughness by reducing the amount of addition. In order to obtain this effect, the addition amount of these elements is preferably set to be less than or equal to the above upper limit; preferably P is 0.020% by weight or less, n is 0.030% or less, and A1 is 0.050% by weight or more. Less '〇' is 0.050 wt0/〇 or less. The oxide or nitride of A1 helps to prevent coarsening of the particles. Therefore, if these elements are too rare, the particles will become thicker and the steel will be tough. In order to reduce the content of these elements in the required amount, the manufacturing cost will be increased; and when these elements reach or fall below certain fixed values, the effect of improving the toughness is saturated, so the content of these elements is preferably set. It is greater than or equal to the above lower limit value. (21) 0.010 wt%^Nb^0.10 wt% ® (22) 0.005 wt%^Ta^〇.l〇wt% (23) 0.005 wt%^Ti^〇.l〇wt% (24) 0.005 wt%^ Zr^0.10 wt% (25) 0.005 wt%^ Mg ^0.10 wt% (26) 0.005 wt%^ REM^0.10 wt%

Nb，Ta，Ti，Zr，Mg及REM每一種均可有效地提升韌性，其中 Nb，Ta，Ti，及Zr係形成微細碳氮化物且藉由顆粒微細化而提升韌 性；而Mg及fEM則藉由減少基質中之氧含量而有效地提升韌性。 為獲得這些效果，這些元素的添加量最好設定於大於或等於 上述下限值；當添加量過大時，將會破壞鋼材之韌性及锻接性， 1358458 故其最好設定在小於或等於上述上限值。 不足，以致破射放電加工性，因= -C之高溫下：之回;金== 度（J·體而5，最尚硬度大於或等於HRC61)。 田鐵之粒彳’故舊沃斯 等於8.0，「顆私j uq马大於或4於3.0以及小於或 其係利請咖中二斯田鐵之粒徑尺寸， 具體度最好大於或等於=小 當吾人在此溫度範圍進行淬火時，即可避免粒 因為本發明基本上傾向於藉由添加S來;^i^*、$+77iiUd_游 故A型包合物會在某-固定範圍内出現，用 :=5⑽之包娜獅咖“士!= 為獲得具有優異加工性之冷作工具鋼，M6() 〇通至L50%之範圍内；「从6〇 χ 4〇〇」意指根據jis 所述之方絲測量之包紗含量，其為初 60 F〇V(^^ ; ^ 最大長度為20 μιη或更小之a型包合物最好伯整體a型包合物 12 1358458 30%比率。 為开4成此一 A型包合物，Μη之添加量必須適合s含量，^ 含量（wt%)最少必須大於或等於S含量（wt%)的17倍；因五 人亦需要Μη來促進可硬化性，故施之添加量通常多^適合as 含量（wt%)之Μη含量（树％)。 因B型包合物及C型包合物（|g、其他氧化物等）不僅會阻 礙改善高速_性質，亦會魏查比鱗值，^者最好可儘量 低，B型包合物及C型包合物意指利用jISG〇555中所述 估計法來蚊之包合物。 叹之^ 口物Each of Nb, Ta, Ti, Zr, Mg and REM can effectively improve the toughness, wherein Nb, Ta, Ti, and Zr form fine carbonitrides and enhance toughness by refinement of particles; and Mg and fEM The toughness is effectively increased by reducing the oxygen content in the matrix. In order to obtain these effects, the addition amount of these elements is preferably set to be greater than or equal to the above lower limit; when the addition amount is too large, the toughness and forgeability of the steel will be destroyed, 1358458, so it is preferably set to be less than or equal to the above. Upper limit. Insufficient, so that the EDM processability, because = -C at high temperature: back; gold == degree (J · body and 5, the most hardness is greater than or equal to HRC61). Tian Tie's granules' old Worth is equal to 8.0, "Peace private j uq horse is greater than or 4 to 3.0 and less than or its profitability, please use the particle size of the second sita iron, the specificity is preferably greater than or equal to = small When we quench in this temperature range, the particles can be avoided because the invention basically tends to be added by adding S; ^i^*, $+77iiUd_ voyage type A clathrate will be within a certain fixed range Appeared, with:=5(10), the bag of lions and lions! = In order to obtain the cold work tool steel with excellent workability, M6() is within the range of L50%; "from 6〇χ 4〇〇" means According to the square yarn measured by jis, it is the initial 60 F〇V (^^ ; ^ maximum length of 20 μηη or smaller a type inclusion complex, preferably the whole a-type inclusion complex 12 1358458 30% ratio. For the addition of 40% of this type A inclusion compound, the amount of Μη must be suitable for the s content, and the content (wt%) must be at least 17 times greater than or equal to the S content (wt%); Μη is required to promote the hardenability, so the addition amount is usually more suitable for the 含量η content (tree%) of the as content (wt%). Because of the B-type clathrate and the C-type clathrate (|g, other oxides) Not only will it hinder the improvement of high speed _ properties, but also the Wei Chabi scale value, which is best to be as low as possible. The B-type inclusion compound and the C-type inclusion compound mean the use of the estimation method described in jISG〇555. Inclusion compound

為獲得具有優異糊性質及耐衝雜之冷作王具鋼 B 具體而言最好小於或等於⑽州；「d (B+C) 6G x働」 ，才曰J，JIS G〇555中所述之方法來測量之B型及c型包合物含 LLli在以働功率光學顯微鏡、6G°F0V (視角）觀察下之包 合物含量。 右古ίΐ將本發明之冷作工具鋼的效果。因為結晶碳化物具 =硬^冷=具鋼之耐磨耗性可藉由分散大量結晶碳化物來 ^，然而，大量結晶碳化料僅會破壞加讀，亦會使線 ===斷裂。結晶碳化物易於成為斷裂之始點，因其顆 性ί;方面，結晶碳化物過少將使得硬度降低、 的旦具鋼中’因在最適化L值時結晶化碳化物 的少，故可提升加m何減少例如線切割放電2 問題，再者’因成為斷裂之始點之粗化結晶碳化物 里已降至取少，且顆粒亦變得微細，故可達到高韌性。 物 要二 =提升在回火溫度—又為 本發明之冷肛_可麵大賊等於HRC 61之硬度，其為 1358458 又 因此，工.In order to obtain a cold-working king steel B with excellent paste properties and resistance to mixing, it is preferably less than or equal to (10) state; "d (B+C) 6G x働", only J, JIS G〇555 The B-type and c-type inclusion complexes measured by the method described above contain the inclusion complex content of LLli under the observation of a 働 power optical microscope, 6G °F0V (viewing angle). The effect of the cold work tool steel of the present invention. Because the crystalline carbide has a hard and cold = the wear resistance of the steel can be dispersed by dispersing a large amount of crystalline carbides. However, a large amount of crystalline carbonized material only destroys the reading, and the line === is broken. The crystalline carbide tends to be the starting point of the fracture. Because of its glutinous properties, the too little crystalline carbide will reduce the hardness, and the denier steel will be improved because it has less crystallization carbides at the optimum L value. Adding m reduces the problem of, for example, wire-cut discharge 2, and further, 'the coarsened crystalline carbide which has become the starting point of the fracture has been reduced to a small amount, and the particles are also fine, so that high toughness can be attained. The second thing is to raise the temperature at the tempering temperature - and the cold anus of the present invention is equal to the hardness of HRC 61, which is 1358458 and therefore, work.

電加,或線切瓶電加4，亦可防止鋼_料毀損/使在放 ，材料易於在尚速範圍（高轉速）加工時鍛接至切削面， 侧二f極易師接部分之反覆形纽分_制賴。在本 ΐίΐ冷作工具鋼中’因&之添加量為大於或等於g.6赠。，不 易發生鍛接情形，及可抑制工具的磨U此，冷作卫 有較I知南速切削鋼為向之可加工性。 * 範例 將具有表1 (範例1至20及比較範例i至10)所示各元素 成之鋼材在高頻真空熔爐中進行熔融。將藉由鑄造而得之鋼堍 施行熱鍛，以形成35 X 55 mm之方形棒；在施行熱鍛後，以7 /hr之冷卻速率自880。(：逐漸地冷卻方形棒來施行球化處理。Electric plus, or wire cut bottle electric plus 4, can also prevent steel _ material damage / make it, the material is easy to forge to the cutting surface in the speed range (high speed) processing, the side two f extremely easy to connect the part Shapes are divided into _ _ _. In the ΐίΐ cold work tool steel, the amount added by & is greater than or equal to g.6. It is not easy to forge the forging situation, and it can suppress the grinding of the tool. The cold working is better than the I know that the south speed cutting steel is suitable for machining. * Example A steel material having the elements shown in Table 1 (Examples 1 to 20 and Comparative Examples i to 10) was melted in a high-frequency vacuum furnace. The steel crucible obtained by casting was subjected to hot forging to form a square rod of 35 X 55 mm; after hot forging, it was cooled from 880 at a cooling rate of 7 /hr. (: The square rod is gradually cooled to perform spheroidization.

14 1358458 表1 妹 T— o o <D g o 03 Z o o m 卜- o ? CO eo 〇 5 o rS g o o 品 § d) CO Ca=0.0049 1 | g ?· A 0 1? 〇> 1 s 0 1 <〇 8 t H- U) cd s r-^ U> CM U9 o CO a> ?; 20.的 5 18.7351 in ts> ui u> Ch u> o CO cd 19.645 u> 〇> cd ▼·· u> p 118.225 u> a> CO s 20.965 u> CM %JD s oi 〇> U£ CM M6.29S CO (O 17.85Ϊ 33.23S ▼— CO 1)28.04! iX3 a> s CO CO CM (O LJ L〇 <〇 r·* c«i <P U) eo ε r"T Si 00 Γ0 2.456 2.4241 CO r*i 00 0> CO (O 穿 cj <〇 CO 0〇 <〇 O) IN 〇» 〇> s g CO o CM CO r> cJ <〇 CO eo 5r »—· c4 s c4 CO CO CO CO CO cr> 0) CM CO 10 r〇 CO o 〇 1 o 1 1 i 1 1 1 1 1 寸 s o o CO i c〇 u> o o' 0.0084 8 o o o δ o o o o 1 i 0.0001 § o o s o 1 s o o o 1 Z 1 1 1 1 1 1 1 1 1 1 I I CO βΜ o T-· o o g o o to o o c〇 s o’ 穿 o o s o o CM »— r-» C3 1 荛 o o 1 s o 1 1 1 < 1 ! 1 1 1 I o o o o s o g o 〇> o U) oo o o' o o 1 机02: 1 to »-· o 1 CO o o > <〇 CM σ> »-· s r"i g· 〇 g r*i CM n* CM c*i o CQ CO d CO eo o o σ Γ- ta o CO o <〇 CO o 04 〇> o CO o CM o CO o o o o o CO ir o ril o CM ° e^> t $ o s o s 1 1 Ί 甚 r> 1 1 H 1 I I 1 I CO \j〇 o 1 s »-· o u> 1 o I 货 o 寸 o V o a> GO OJ CM CO CO CO CO LA w 〇> u> 〇> CO lO 〇> CO OO oi Oi CO csi 这 oi in CO r«i CO 〇> c\i r^- cJ CO esi CO oi s c4 CO ^*4 〇> CO o CO o α» o 〇» = oo 0 01 & Ψ"· CM ·** ώ U3 «〇 P in CO 卜 s CO o oo CNl <〇 <〇 <〇 CO 寸 <〇 a> CO o CO «〇 CO to (O <d CO 〇> in CO o CO LA 卜: <£> T-· CO CO lO <d CRl <〇 CM (O b CO CO csi V*· s V-· V· CO o GO cd er> S 1 1 〇 s o g o CO CM 〇 S 〇 〇> CO o r- o s o s o’ CO o c*> o o 1 1 o 1 1 o 1 5 1 1 CO σ s o CO O S o V· o CM o CO CO o’ CM o co CM o CM o i o 1 eo o OI o 1 (0 IA CO o in CO o CO g CO lO 寸 a> ο rS cr> o <S CO \Si o ri ΓΟ oo o o to 〇 o r^· d o o CO %〇 o o oo 呂 o GO 呂 o CO g o 5 o g o Γ7 s o ό o o o o o o o g o g o o o o o Τ Ο a. 1 1 1 1 1 1 1 1 1 I I r^· 8 O 寸 8 s o o 〇> s o o CO o 1 1 1 s o 3 o 5 o 1 o 1 CO in u> CM CO CO «〇 CO (O CO CO οι 〇> 〇 GO O) 〇 <M T— 〇 s rS CO IM 〇 〇 Hi o CM OJ o o 〇 Q o o CO CO o σ> CO o ID CO o CO o t_> o «μ o # oo ° o eM o CO o «〇 u> CO o r- 罟 oo CO Oi s CM CM CO CO in eo GO r-· 〇> 3 LO 〇» o s o CO GO o 〇> CO o CO CM ·"· a> o ΐα» o eo o cy o CO o CM o (O o 〇> o CO V·» oo o CO o ο r- <〇 〇> oo ° o CO CO c〇 卜 CM <〇 〇 s 〇 〇 CO 〇 00 CO CO oo o 〇 o to «0 o LO 卜 o o CO o CO 00 o (A oo o o s CO <〇 o 〇> <〇 o lii 卜 o o CO c!l V-· C4 寸 LA <〇 CO Oi V r— csl CO \X> <〇 卜 cO 〇» CM CO o14 1358458 Table 1 Sister T— oo <D go 03 Z oom 卜 - o ? CO eo 〇5 o rS goo § d) CO Ca=0.0049 1 | g ?· A 0 1? 〇> 1 s 0 1 <〇8 t H- U) cd s r-^ U> CM U9 o CO a>?; 20. 5 18.7351 in ts> ui u> Ch u> o CO cd 19.645 u>〇> cd ▼· · u> p 118.225 u>a> CO s 20.965 u> CM %JD s oi 〇> U£ CM M6.29S CO (O 17.85Ϊ 33.23S ▼—CO 1)28.04! iX3 a> s CO CO CM ( O LJ L〇<〇r·* c«i <PU) eo ε r"T Si 00 Γ0 2.456 2.4241 CO r*i 00 0> CO (O wear cj <〇CO 0〇<〇O) IN 〇» 〇> sg CO o CM CO r> cJ <〇CO eo 5r »—· c4 s c4 CO CO CO CO CO> 0) CM CO 10 r〇CO o 〇1 o 1 1 i 1 1 1 1 1 inch soo CO ic〇u> oo' 0.0084 8 ooo δ oooo 1 i 0.0001 § ooso 1 sooo 1 Z 1 1 1 1 1 1 1 1 1 1 II CO βΜ o T-· oogoo to ooc〇s o' Wear oosoo CM »- r-» C3 1 荛oo 1 so 1 1 1 < 1 ! 1 1 1 I oooosogo 〇> o U) oo o o' oo 1 02: 1 to »-· o 1 CO oo ><〇CMσ> »-· s r"ig· 〇gr*i CM n* CM c*io CQ CO d CO eo oo σ Γ- ta o CO o <〇CO o 04 〇> o CO o CM o CO ooooo CO ir o ril o CM ° e^> t $ osos 1 1 Ί rr> 1 1 H 1 II 1 I CO \j〇o 1 s »-· o u> 1 o I goods o inch o V o a> GO OJ CM CO CO CO CO LA w 〇>u>〇> CO lO 〇> CO OO oi Oi CO Csi this oi in CO r«i CO 〇> c\ir^- cJ CO esi CO oi s c4 CO ^*4 〇> CO o CO o α» o 〇» = oo 0 01 &Ψ"· CM ·** ώ U3 «〇P in CO 卜 s CO o oo CNl <〇<〇<〇CO inch<〇a> CO o CO «〇CO to (O <d CO 〇> in CO o CO LA Bu: <£> T-· CO CO lO <d CRl <〇CM (O b CO CO csi V*· s V-· V· CO o GO cd er> S 1 1 〇sogo CO CM 〇S 〇〇> CO o r- osos o' CO oc*> oo 1 1 o 1 1 o 1 5 1 1 CO σ so CO OS o V· o CM o CO CO o' CM o co CM o CM oio 1 eo o OI o 1 (0 IA CO o in CO o CO g CO lO inch a> ο rS cr> o <S CO \Si o ri ΓΟ oo oo to 〇or^· doo CO %〇oo oo 鲁o GO 鲁o CO go 5 ogo Γ7 so ό ooooooogogooooo Τ Ο a. 1 1 1 1 1 1 1 1 1 II r^· 8 O inch 8 soo 〇> soo CO o 1 1 1 so 3 o 5 o 1 o 1 CO in u> CM CO CO «〇CO (O CO CO οι 〇> 〇GO O) 〇<MT_ 〇s rS CO IM 〇〇Hi o CM OJ oo 〇Q oo CO CO o σ> CO o ID CO o CO o t_> o «μ o # oo ° o eM o CO o «〇u> CO o r- 罟oo CO Oi s CM CM CO CO in eo GO r-· 〇> 3 LO 〇» oso CO GO o 〇> CO o CO CM ·" · a> o ΐα» o eo o cy o CO o CM o (O o 〇> o CO V·» oo o CO o ο r- <〇〇> oo ° o CO CO c〇 CM < 〇〇s 〇〇CO 〇00 CO CO oo o 〇o to «0 o LO oo CO o CO 00 o (A oo oos CO <〇o 〇><〇o lii oo CO c!l V -· C4 inch LA <〇CO Oi V r- csl CO \X><〇卜cO 〇» CM CO o

各元素組成係以「重量百分率」（wt%)來表示；K值及L值 亦同。 15 1358458 结七生之鋼材產品均受到加工性測試（端銑加工測試）、 ΐΐ Λ 試、硬度料、航_職、社後顆粒尺 寸Gq、以及包合物含量估計。 加工性職（麟加工測試）係施行至在球化退火狀 材產品切割下來之一測試片。測試條件如下： 態自鋼The composition of each element is expressed in terms of "percentage by weight" (wt%); the K value and the L value are also the same. 15 1358458 The seven steel products are all subjected to the processability test (end milling test), ΐΐ Λ test, hardness material, aviation _ occupation, post-particle size Gq, and inclusion composition estimation. The processing job (Lin Processing Test) is applied to one of the test pieces cut in the spheroidized annealed product. The test conditions are as follows: State from steel

工具：燒結碳化物（cementedearbide) M2〇 ( 0 32m 速率：200m/min 饋入速率：0.15 mm/rev 切削寬度：4.5 mm 切削向度：1.2 mm 切削油：無 工具壽命：在刀具侧腹部之最大磨耗量達〇 3胃時之切削距 離 估計方法·以比較工具鋼1號之工具壽命作為1〇〇之相對估 計 、線切割放電加工測試係根據下列不驟來施行。簡言之，自球 化退火鋼材切割出一 30 X 50χ 200 mm測試片，將測試片在一預 定條件下淬火並回火；於該測試片上鑽出0 4 mm的孔洞後，測 試片即利用線切割放電加工鑿成10 χ 2〇 mm之方形狀；在施行放 電加工後，令測試片豎立一天，測量測試片上所產生之裂縫數目。 在硬度方面，自球化退火鋼材切割出一 2〇 χ 20 mm之片狀測 試片，在一預定溫度下量測淬火及回火後之硬度；測量在表2所 示之特定溫度下回火之數值（測試硬度）以及在1〇〇至6〇〇。〇下回 火之最大值（最高硬度）。 在室溫下’對在一預定溫度下淬火及回火後而形成自球化退 火鋼材之10R-缺口狀查比衝擊測試片施行查比衝擊測試，取三測 試片之平均值做為衝擊值。 顆粒尺寸Gq係根據JIS G0551中所述之方法來測量。A型包 合物及(B+C)型包合物之包合物含量係利用JISG0555中所述之方 1358458 法來測量（光學顯微鏡放大倍率：400，視角數：60)。 ^ 表2顯示淬火溫度、回火溫度、以及各種不同估計測試之，·< 果，L值與結晶碳化物量間之關係則顯示於圖1° 表2Tool: cementedearbide M2〇 (0 32m rate: 200m/min Feed rate: 0.15 mm/rev Cutting width: 4.5 mm Cutting dimension: 1.2 mm Cutting oil: no tool life: maximum on the cutter side abdomen The method of estimating the cutting distance when the wear amount reaches 胃3 stomach·The relative estimation of the tool life of Tool Steel No. 1 is 1 〇〇, and the wire-cut electrical discharge machining test system is carried out according to the following steps. In short, self-spheroidization The annealed steel cut a 30 X 50 χ 200 mm test piece, and the test piece was quenched and tempered under a predetermined condition; after the hole of 0 4 mm was drilled on the test piece, the test piece was cut into 10 by wire-cut electrical discharge machining. χ 2〇mm square shape; after performing electrical discharge machining, the test piece is erected for one day, and the number of cracks generated on the test piece is measured. In terms of hardness, a 2 〇χ 20 mm sheet test is cut from the spheroidized annealed steel. The sheet was measured for hardness after quenching and tempering at a predetermined temperature; the value of tempering at a specific temperature shown in Table 2 (test hardness) was measured and at 1 to 6 Torr. most Value (highest hardness). Perform a Charpy impact test on a 10R-notched Charpy impact test piece that forms a self-spheroidizing annealed steel after quenching and tempering at a predetermined temperature at room temperature, taking three test pieces. The average value is taken as the impact value. The particle size Gq is measured according to the method described in JIS G0551. The inclusion complex content of the type A clathrate and the (B+C) type clathrate is determined by the method described in JIS G0555. 1358458 Method to measure (optical microscope magnification: 400, number of viewing angles: 60). ^ Table 2 shows the quenching temperature, tempering temperature, and various different estimation tests, · < fruit, the relationship between the L value and the amount of crystalline carbide It is shown in Figure 1° Table 2

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Gong β • φ -ο C^J oo r-^ 〇oosoosooooooo' oo CO oooosoo 〇O o CM oo O o Ο Ο iasoogoo CO »— o »* oo CO ο oo Ο S 〇ό 4° φΐ CO CM o in CO oo CO CM CO O) o CO o a> OJ oao L£> o CO CO o CO <〇CO u> in CO ΙΑ 3 <〇CO <〇CM Ο c〇o' Goo Ol od tA CM 〇(O CO oc; o ο o' CM 〇〇〇> oos ο in ό CO φ a> 黯5 <〇〇〇卜Ui 卜tn CO <〇CO oo CO Mi σ>兮〇» oo (O inch CO a* U) 〇> CO CO CM ο» CO 00 CO LA <〇in σ> CO CO LO Uu U> CO CO ΙΛ CO Oi co in CO CSI CO P; LA CO % in lifting CO r> is CM to CO CM CO σ> CO a> Ol —, Μ 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举 举; God 1 target lOiJ w 蜊ifh > »w 璲*w wall*w let _ * £ &u> O) oo CO art CO oo CNJ <〇GO a CM CO oo CM s; CM s CO 5 CO σ>σ> »— m 〇>& V*· (O m C O s § 8 ίΟ CM CO CO w^· W-^ 〇><〇CO CO U) <〇ST— Sg ^ X mwc» ύ • CM <〇r—CO <〇CO ύ c4 ( O ύ oi 〇*i <〇CSl oi <〇ύCJ ύ Oi CO CO «Μ csi <〇寸〇i <〇c\i <〇ca 04 <〇〇> GO ύ CM oi <〇eo σί u> £ ci 卜 (Ο in CO 〇> m CNl σ> LA inch cd u> ύ τ — <£> ^ y 泛 i CO c*i (C> CO ci u> CO 04 c4 5 c〇CO <0 00 01 «0 c*><6 «Ρ CM csi «Ρ a> c〇(P 〇>卜<〇ύ CO s GO CO to c〇CO &lt ;〇»— cvl CD ci cri CD C〇〇> ύ c*S 卜cb ΙΑ Oi f6 CP CO t6 to CJ (0 GO c\i 4 oso CM IO oao IA o rj s in o φ 〇1 ozo u&gt Oso ο CM U> o » osss IA o 笃s ir> 〇 IA oso LA OJ os ο wear o wear oa 〇〇s 2Λ sot- u> oooooo 〇>σ> another osomo 毋ο so 〇so u> CM o CM LA oc〇〇o u> so tE § o r-iso o 00 8 o 〇> S m CO o nest o CM so CO so ο ο U) ao lA 〇r- s T- 〇 ο ο 骧^ v-» •v^ L3 5 17 1358458 As shown in Figure 1, there is a relationship between the L value and the amount of crystalline carbide, and when the L value exceeds 21.0, the amount of crystalline carbide exceeds 4 〇 plus % . In the comparative example. 犮 6 to 10, the L value of each of the examples is extremely large, so the amount of crystalline carbide is large. Therefore, the impact value of the steel material is poor in workability; _ is Comparative Examples 7 and 8, wire-cut discharge plus. The work caused the line to break; in Comparative Examples 3, 9 and 1G, the tempering temperature was lower than 45 〇c, and the fracture occurred after the electric discharge machining; in addition, in Comparative Examples 2, 4 and 5, the maximum hardness was less than HRC. 6 Because the alloying elements, Mg, and v are not within the scope of the present invention; in Comparative Example 6, since the κ value is too large, sufficient secondary hardening cannot be achieved, and the maximum hardness is less than HRC61. The steels (examples) U of the present invention each have a maximum hardness of greater than or equal to (4) 61 because the κ value, the L value, and each of the other alloying elements have been optimized, so that it exhibits excellent reinforcement. And the discharge of the ten-year-old South Hengqing value. Fig. 2 shows the relationship between the amount of Si added and the workability, in which the processability is remarkably improved when it is contained, and the original 13 is that the abrasion of the tool due to the forging is suppressed by the addition of a predetermined amount of Si. The present invention has been described in detail above; however, the present invention is by no means limited to only == real_', without departing from the gist of the present invention, the present invention can be used for various different types of steel. Cold tilting and various five. [Simple description of the drawing] Figure 1 shows the relationship between the L value and the crystalline carbide content; and Figure 2 shows the relationship between the Si content and the processability. [Main component symbol description]

Claims (1)

1358458 100年8月2日修正替換頁 申請專利範圍·· 一' 1. 一種冷作工具鋼’包含： 丨p年月之曰本 0.4SK 值(κ 值=Cr (wt%) - 6.8 C (νη%)); 15,5^L (L ^t = Cr (wt%)+ 15.5 C(wt%)); 0.60 wt%< Si^2.0 wt% ； ’ 0.10 wt%^Mn^ 1.0 wt〇/〇 ； 0.041 wt%SS^0.2 wt°/〇 ； 1.25 wt°/〇<Mo + 0.5 W<3.0wt°/〇 ； 0.05wt%SVSl.〇wt% ;以及 剩餘部分Fe與無可避免之雜質； 我在眞或更高溫度下回火所得之最大硬度 為HRC 61或更大值； 其中該冷作工具鋼具有〇.l〇%SdA 60 X 400S1.50%，其中 「dA 60 X 400」為根據nS G0555中所述之方法進行量測之包合物， 含量；以及 。該冷作工具鋼能夠藉由在大於或等於95(rc及小於或等於 1080°C之溫度下淬火，且3.〇sGqg8 〇來獲得，苴中「G 火後的舊沃斯田鐵之頭粒尺寸，其係根據G〇551中所述之方法 進行測量。 2. 如申請專利範圍第1項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.005 wt%^Se^〇.l〇 wt% ； 0.005 wt%^Te^0.1〇wt% ; 0.0002 wt%^Ca^0.010 wt% ; 0.005 wto/oSPbSO.lOwto/o ;以及 0.005 wt%SBi^〇.l〇wt%。 3. 如申請專利範圍第i項之冷作鋼 擇自下列條件之元素： 八調又u狀少、 〇.〇1 wt%^Cu^2.0 wt% ; 19 “58458 '1 100年8月2曰修正替換頁 94115562(無劃線）' 0.01 wt%^Ni^2.0 wt% ； -- 〇.20wt%SCo$1.0wt% ;以及 0.0003 wt%SBS0.010 wt%。 4.如申請專利範圍第2項之冷作工具鋼，更包含一或更多撰 4¾ r ^ ^ 释自下列條件之元素： 0.01 wt%^Cu^2.0 wt% ； 0.01 wt%^Ni^2.0 wt°/〇 ； 0.20wt〇/〇SC〇S1.0wt% ;以及 0.0003 wt%$B$0.010 wt%。 s.如申請專利範圍第1項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.0010 wt°/〇^P^0.030 Wt% ； 0.0050 wt%^N^0.050wt% ； 0.0010 wt%$Al$0.10 wt% ;以及 0.0002 wt%$〇$〇.〇l〇 wt%。 6. 如申請專利範圍第3項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.0010 wt°/〇^P^0.030wt% ；1358458 Correction of the replacement page on August 2, 100, the scope of application for patents ·· 1. A cold work tool steel' contains: 0.4p year and month 曰 0.40.4 value (κ value = Cr (wt%) - 6.8 C ( Ηη%)); 15,5^L (L ^t = Cr (wt%) + 15.5 C (wt%)); 0.60 wt% < Si^2.0 wt% ; ' 0.10 wt%^Mn^ 1.0 wt〇 /〇; 0.041 wt% SS^0.2 wt ° / 〇; 1.25 wt ° / 〇 < Mo + 0.5 W < 3.0 wt ° / 〇; 0.05 wt% SVSl. 〇 wt%; and the remaining part of Fe and unavoidable Impurity; The maximum hardness I get from tempering at helium or higher is HRC 61 or greater; where the cold work tool steel has 〇.l〇% SdA 60 X 400S1.50%, where "dA 60 X 400 The content of the clathrate, as measured according to the method described in nS G0555; The cold work tool steel can be obtained by quenching at a temperature greater than or equal to 95 (rc and less than or equal to 1080 ° C, and 3. 〇sGqg8 〇, the head of the old Worthite iron after the fire in the 苴The particle size, which is measured according to the method described in G. 551. 2. The cold working tool steel according to claim 1 of the patent application further contains one or more elements selected from the following conditions: 0.005 wt% ^ Se ^〇.l〇wt%; 0.005 wt%^Te^0.1〇wt%; 0.0002 wt%^Ca^0.010 wt%; 0.005 wto/oSPbSO.lOwto/o; and 0.005 wt%SBi^〇.l〇wt% 3. If the cold work steel of the application scope of item i is selected from the following conditions: eight tones and less u, 〇.〇1 wt%^Cu^2.0 wt%; 19 “58458 '1 August 100 2曰Correct replacement page 94115562 (without scribe line)' 0.01 wt%^Ni^2.0 wt% ; -- 〇.20wt%SCo$1.0wt% ; and 0.0003 wt% SBS0.010 wt%. 2 items of cold work tool steel, including one or more elements of 43⁄4 r ^ ^ from the following conditions: 0.01 wt%^Cu^2.0 wt%; 0.01 wt%^Ni^2.0 wt°/〇; 0.20wt 〇/〇SC〇S1.0wt%; and 0.0003 wt%$B$0.01 0 wt%. s. For cold working tool steel according to item 1 of the patent application, one or more elements selected from the following conditions: 0.0010 wt°/〇^P^0.030 Wt%; 0.0050 wt%^N^ 0.050 wt%; 0.0010 wt%$Al$0.10 wt%; and 0.0002 wt%$〇$〇.〇l〇wt%. 6. For cold work tool steel according to item 3 of the patent application, one or more options are included. Elements from the following conditions: 0.0010 wt ° / 〇 ^ P ^ 0.030 wt%; 0.0050 wt°/〇^N^0.050wt% ； a〇〇l〇wt%SAlS0.10wt% ;以及 0.0002 wt0/〇S〇$〇.〇l〇 wt%。 7. 如申請專利範圍第4項之冷作工具鋼，更包含—或更多選 释自下列條件之元素： 0.0010 wt%^P^〇.〇3〇wt% ； 0.0050 wt°/〇^N^0.050wt% ； 0.0010 wt%$Al$0.10 wt% ;以及 0.0002 wt0/〇$〇$〇.〇l〇 wt%。 更包含一或更多選 8·如申請專利範圍第6項之冷作工具鋼 擇自下列條件之元素： 1358458 _ .' 100年8月2曰修正替換頁 .| | 94115562(無劃線） 0.010 wt%^Nb^0.10wt% ； 0.005 wt%^Ta^0.10wt°/〇 ； 0.005 wt%^Ti^0.10 wt% ； 0.005 wt%^Zr^0.10 wt% ； 0.005 wt%$Mgg0.10 wt% ;以及 0.005 wt%SREMS0.10 wt%。 9.如申請專利範圍第7項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.010 wt%^Nb^0.10 wt% ； 0.005 wt%$Tag0.10 wt% ; ® 0.005 wt%^Ti^0.10 wt% ； 0.005 wt°/〇^Zr^0.10 wt% ； 0.005wt%刍MgSO.lOwt% ;以及 '. 0.005 wt%g REM $0.10 wt%。 H—、圖式：0.0050 wt°/〇^N^0.050wt%; a〇〇l〇wt%SAlS0.10wt%; and 0.0002 wt0/〇S〇$〇.〇l〇 wt%. 7. For cold-work tool steels in the scope of patent application No. 4, further include – or more elements selected from the following conditions: 0.0010 wt%^P^〇.〇3〇wt%; 0.0050 wt°/〇^N ^0.050wt%; 0.0010 wt%$Al$0.10 wt%; and 0.0002 wt0/〇$〇$〇.〇l〇wt%. More includes one or more options. 8. The cold-work tool steel as in item 6 of the patent application is selected from the following conditions: 1358458 _ .' 100 years August 2 曰 revised replacement page. | | 94115562 (without line) 0.010 wt%^Nb^0.10wt%; 0.005 wt%^Ta^0.10wt°/〇; 0.005 wt%^Ti^0.10 wt%; 0.005 wt%^Zr^0.10 wt%; 0.005 wt%$Mgg0.10 wt % ; and 0.005 wt% SREMS 0.10 wt%. 9. For cold working tool steel according to item 7 of the patent application, one or more elements selected from the following conditions: 0.010 wt%^Nb^0.10 wt%; 0.005 wt%$Tag0.10 wt%; ® 0.005 Wt%^Ti^0.10 wt%; 0.005 wt°/〇^Zr^0.10 wt%; 0.005 wt% 刍 MgSO.lOwt%; and '. 0.005 wt% g REM $0.10 wt%. H—, schema: 21 135845821 1358458 0.1 1 Si 量（wt%) o.o 0.010.1 1 Si amount (wt%) o.o 0.01 丄 10 圖2丄 10 Figure 2