TW200536945A - Cold work tool steel - Google Patents

Abstract

Cold work tool steel of the present invention comprises 0.4 ≤ K value ≤ 2.6 (K value=Cr(wt%)-6.8C(wt%)), 15.5 ≤ L value ≤ 21.0 (L value=Cr (wt%)+15.5 C (wt%)), 0.60 wt% < Si ≤ 2.0 wt%, 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% ≤ V≤ 1.0 wt%, and the balance Fe and inevitable impurities, in which the highest hardness obtained by tempering at 450 DEG C or higher after quenching is HRC 61 or more.

Description

200536945 九、發明說明： 一、【發明所屬之技術領域】 作工合各綱冷模之冷 冷锻模、型鋪、螺紋滾 '(製）、-曲模、 框下料模、量規、深引伸衝頭 牛义開縫刀具、引線 曲模、引伸模、冷顧塑性加工工且、、二用2刀二二銹鋼、響 件混 ：；i^ CVD^ 二、【先前技術】 材作=量上，沐 ’可增強以JIS鋼 耗性或耐擦i性之各種不耐磨 上;然而，習知冷作工具鋼仍===:、冷鍛模等） =件硬化等將削弱模具硬度；及⑶線斷 如引出各鮮狀方法轉決這些問題，例 =H利1揭路-種冷作工具鋼，包含C: 〇 75至175 ^ 至 3.0 wt%、Mn: (U 至 2.〇 Μ%、Cr: 5 〇 至 u 〇 加％、M〇q 3 hardness)來大幅提升工具壽命及放電加工性。 引證專利2揭露-種具有一預定組成之冷作工具鋼，盆 1〇〇 μιη或更小之碳化齡聚部分之黏聚尺寸；引證專利2亦^露 200536945 碳化物之斷裂及其可藉由將 以抑制，以延長工具壽命。來尺寸投定在1〇〇 μπι或更小而加 引口豆專利3揭露一種具有一^ 其中α值卜〇·706 + 〇 541 c、 二疋、、且成之高硬度冷作工具鋼， 至 1.0，且β值（=廳當量 +19 施-0.232 V)為 0.7 3亦說_劣碳化物及黏聚碳化；引證專利 在這些翻㈣善與硬絲層此可糾將謹及β值設定 引。丑專利4揭鉻一種具有一預定組成之古廊声Α你丁 其中5〜35 ν〇1·〇/0之殘留沃斯田鐵（&amp; 同^ 八鋼，200536945 IX. Description of the invention: 1. [Technical field to which the invention belongs] Cold forging die, profile shop, thread rolling '(manufacturing), -curve die, frame blanking die, gauge, deep Extension punch Niu Yi slitting tool, lead curve die, extension die, cold-looking plastic processing tools, and two with two knives and two two rust steels, and two parts: i ^ CVD ^ Second, [previous technology] material = In terms of quantity, Mu 'can enhance various non-wear resistance based on JIS steel wear resistance or abrasion resistance; however, the conventional cold work tool steel is still === :, cold forging dies, etc.) = Piece hardening, etc. will weaken Mold hardness; and ⑶ wire breaks, such as fresh-cut methods to resolve these problems, for example = H Lee 1 open the road-a kind of cold work tool steel, including C: 〇75 to 175 ^ to 3.0 wt%, Mn: (U to 2. 0%, Cr: 50% to 50%, and molq 3 hardness) to significantly improve tool life and EDM. Citation Patent 2 discloses a cohesive size of a cold-working tool steel with a predetermined composition and a carbonized age-aggregated portion of 100 μm or less; Citation Patent 2 also discloses 200536945 carbide fracture and its use. Will be suppressed to extend tool life. The size is set at 100 μm or less and the pea patent 3 discloses a high-hardness cold-worked tool steel with a value of α ^ 706 + 541 541 c, 疋, and, To 1.0, and β value (= hall equivalent +19 applied -0.232 V) is 0.7 3 also said _ inferior carbide and cohesive carbonization; cited patents can be corrected in these good and hard layers and β value Set the lead. Ugly Patent 4 Reveals Chromium An Ancient Gallery Sound A Ni Ding with a Predetermined Composition 5 ~ 35 ν〇1 · 〇 / 0 Remaining Vostian Iron (&amp; same as ^ Bagang,

0.01 1. 2 μιη 埒旦』刀欣考’ W證專利4亦說明藉由均勻分 月丈預疋置之殘留沃斯田鐵可提升抗疲勞性。 1刀 ί：3ΐΗ??ί^ [引證專利1]日本專利申請案公開號859_179762 [引證專利2]日本專利申請案公開號2〇〇2_12952 [引證專利3]日本專利申請案公開號2〇〇〇_〇73142 [引迅專利4]曰本專利申請案公開號2004-035920 [引證專利5]日本專利申請案公開號2〇〇〇_355737 #實，模具以及小產品編號之模具特別要求優異可加工性更甚 於杈具哥命，簡言之，某些使用情況需要可確保1111(：6〇或更大硬 度之冷作工具鋼，HRC 60者可在保有以任何加工方法（包含切 削、放電加工、以及線切割放電加工）之加工簡易性下仍具盘 一般模具相同之硬度。 ^然而，以SKD 11來表示之習知冷作工具鋼，即使在退火狀 態下仍存在加工性極差的問題，因為結晶石炭化物係大量分散以期 確保預定之耐磨耗性；又，在線切割放電加工時，結晶碳化物常 引發線斷裂。0.01 1. 2 μιη "Dan Xin Kao" W certificate patent 4 also shows that by evenly dividing the residual Vostian iron installed in advance, the fatigue resistance can be improved. 1 knife: 3ΐΗ ?? ^ [Citation Patent 1] Japanese Patent Application Publication No. 859_179762 [Citation Patent 2] Japanese Patent Application Publication No. 0022_12952 [Citation Patent 3] Japanese Patent Application Publication No. 200 〇_〇73142 [Citation patent 4] Japanese Patent Application Publication No. 2004-035920 [Citation Patent 5] Japanese Patent Application Publication No. 2000-355737 #Actually, molds and molds with small product numbers have excellent requirements Machinability is more important than cutting. In short, some use cases require a cold-working tool steel that can ensure a hardness of 1111 (: 60 or greater). HRC 60 can be retained by any processing method (including cutting , Electrical discharge machining, and wire cutting electrical discharge machining) still have the same hardness as the general mold of a disk. ^ However, the conventional cold work tool steel represented by SKD 11 has extremely high workability even in the annealed state. The problem is poor because the crystalline stone carbides are dispersed in large amounts in order to ensure a predetermined abrasion resistance. Moreover, during wire cutting and electrical discharge machining, crystalline carbides often cause wire fractures.

200536945 吾人亦已知其中結晶碳化物量被減少至 材料；然而，在此習知材料中，高溫回火時吾夂難 HRC 60或更大硬度。另—方面，觀確保可運 硬1時，淬火時在材料中所產生之應力便無法工口5獲= 得之材=施行放電加卫或線切割放電加工;，=應= 月b失去平衡而導致材料之斷裂或毁損。 ”心 量專^ 之冷作工具鋼中，因其結晶碳化物減少 夕 成會受_整’如此可確保聽⑼或更大 硬度，且可加讀可提升至某些程度；然而，即使在引證專利i200536945 We also know that the amount of crystalline carbides is reduced to the material; however, in this conventional material, it is difficult for us to temper HRC 60 or greater when tempered at high temperatures. On the other hand, to ensure that it can be transported for 1 hour, the stress generated in the material during quenching cannot be obtained. 5 = = obtained material = electrical discharge guarding or wire cutting electrical discharge machining ;, = should = month b loses balance As a result, the material is broken or damaged. "In cold work tool steels with special weights, due to the reduction of crystalline carbides, they will be affected." This can ensure the hardness or greater hardness, and can be read to improve to a certain degree; however, even in Citation Patent i

St冷中，可加工性之改良仍嫌不足。至』證專 利2至5亚未揭路在保有高硬度時可改良可加讀之具體裝置。 三、【發明内容】 本發明之目的於是在於提供回火後具有6〇或更大硬度 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：04^κ值g2.6 (κ值=(:1&gt; (wt%) - 6.8 C (wt%)) ； 15.5^L ^^21.0 (L ^ = Cr (wt〇/〇) + 15.5 C (wt/〇)) ； 0.60 wt〇/〇&lt;Si^2.0 wt〇/〇 ； 0.10 wt〇/〇^Mn^L0 wt〇/〇 ； 0.03 wt/〇&lt;S^0.2 wt% , 1.25 wt%&lt;Mo +0.5 W&lt;3.0wt°/〇 ； 0.05 wt%^ 以，剩餘部分Fe與無可避免之雜質，其中藉由泮火 {在450 c或更咼溫度下回火所得之最大硬度為HRC 61或更大 值0 根據本發明之冷作I具鋼，因&amp;健設定於—献範圍，故 —HRC 61，更大值之尚溫回火後可得一最大硬度；因[值係固 疋於預疋範圍，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之外另加入〇.6wt%或更多的si，故 可獲得等同於或優於習知高速_鋼材之加工性。 四、【實施方式】 200536945 效將相況明本發明之較佳實施例 含下列元素、剩餘部分Fe與無可避免m冷作工具鋼包 組成範圍及其限制理由如下所示。i ’待添加之元素種類、 ⑴0.4SK 值S2.6 (K 值=Cr (wt%) _ 6 8 c ( K值表示在適料火溫度下基f巾之殘餘^* 於〇·4或大於2.6時，即降低了所形成之有助於二虽K值小 碳化物量’以致於45(TC或更高温度的、择^二^欠硬化之 或更大值之鋼材；又κ值最好為大於或特為= 2.5 ’若為大於或等純6及小於或等於2 4則更佳。，】、於或雜 W^i 5-~L ^~2L〇 (L ^^^(^/0)+15.5 C (wt%)) 含量俞多之含量；L值歧，結日^化物之 ㈣僅f為結晶碳化物不易形成， ί則I即表示結晶碳化物含量過度地增加，如In the cold, the improvement of workability is still insufficient. The patents 2 to 5 of the “To” certificate can improve the specific device that can be read while maintaining high hardness. 3. [Summary of the Invention] The object of the present invention is to provide a cold-worked tool steel having an excellent workability of 60 or more hardness after tempering. The cold work tool steel according to the present invention includes: 04 ^ κ value g2.6 (κ value = (: 1 &gt; (wt%)-6.8 C (wt%)); 15.5 ^ L ^^ 21.0 (L ^ = Cr ( wt〇 / 〇) + 15.5 C (wt / 〇)); 0.60 wt〇 / 〇 &lt; Si ^ 2.0 wt〇 / 〇; 0.10 wt〇 / 〇 ^ Mn ^ L0 wt〇 / 〇; 0.03 wt / 〇 &lt; S ^ 0.2 wt%, 1.25 wt% &lt; Mo +0.5 W &lt; 3.0wt ° / 〇; 0.05 wt% ^, the remaining part of Fe and unavoidable impurities, where by the flame {at 450 c or 咼The maximum hardness obtained by tempering at temperature is HRC 61 or greater. 0 The cold work I steel according to the present invention is set to the-range, so-HRC 61, the greater value is still tempered. A maximum hardness can be obtained; because the value is fixed in the pre-cranking range, the processability can be improved, and the break of the wire on the wire cutting EDM can be suppressed; furthermore, in addition to s, 0.6 wt% or more More si, so it can obtain the workability equal to or better than the conventional high-speed steel material. [Embodiment] 200536945 The effect will show that the preferred embodiment of the present invention contains the following elements, the remaining Fe Avoidance of the ladle composition range of m cold work tools and its limitation It is shown below. I 'Type of element to be added, ⑴0.4SK value S2.6 (K value = Cr (wt%) _ 6 8 c (K value represents the residue of the base f towel at a suitable fire temperature ^ * in When 0.4 or greater than 2.6, the amount of small carbides that contribute to the K value, although small, is reduced to 45 ° C or higher, and the steel is selected to be underhardened or greater; The κ value is preferably greater than or particularly = 2.5 'It is more preferable if it is greater than or equal to pure 6 and less than or equal to 2 4.,], Or or W ^ i 5- ~ L ^ ~ 2L〇 (L ^ ^^ (^ / 0) +15.5 C (wt%)) content Yu Duo's content; L value is different, the last day of the compound is only f is not easy to form crystalline carbides, I means excessive crystalline carbide content To increase, such as

Ξ ίίϊϊίΓ&quot;7 J '同之顆粒尺寸；L值大於或等於15.8且小於或 $日日日碳化物意謂圓形對應直徑 οΠΐ .Iff 1〇 μιη之碳化物’主要由M?C3來代表（M代表 碳化物^ ’ ·线〇之L值即對應於〇.20至4.〇Wt%之結晶 (3) 0.60 wt% &lt; Si^2.0 wt% ㈣^ = 系加入作為去氧化元素，故其通常包含於鋼材内。在本 嗌月中，吾人主動添加Si以輔助切削；因添加別可獲得之改良加 =性不僅只發生於退火後之低硬度（約^^95)狀態，亦發生於 回火後之高硬度狀態（HRC61或更大），添加义亦有助於 改良南溫回火硬度。 為獲得此一效果，必須添加超過〇·6 含量之si，即使再過 200536945 虿添加Si，但效果已達飽和，因此，Si含量最好設定於2.0 wt%或 更低；又矽含量為〇·65 wt%或更大以及ι·8 wt%或更小較佳，若為 〇,7wt%或更大以及ι·5 wt%或更小則更佳。 (4) 0.10 wt%^Mn^ 1.0 wt% 、，_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添加量為〇·1〇 wt%或更多；當 過量添加Μη時，即破壞了熱加工性，因此，Mn含量最好為1〇加％ 或更低。 (5) 0.03 wt% ^ S ^ 0.2 wt% S為一高速切削元素，其會與]^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（取。 61或更大）。 為獲得此一效果，必須添加0 03加％或更多含量之s，當過量 添加s時，材料區塊中之查比衝擊（Chaipy impact)值將大幅衰 減’因此，Si含量最好設定於〇·2 或更低。 (6) 1.25 wt%&lt;Mo + 0.5 W&lt;3.0 wt%7 ίίϊϊίΓ &quot; 7 J 'Same particle size; L value is greater than or equal to 15.8 and less than or equal to the diameter of the carbide means the corresponding diameter of the circle οΠΐ. Iff 10μm of carbide' is mainly represented by M? C3 ( M represents the carbide ^ '. The value of L in line 0 corresponds to the crystal of 0.20 to 4.0 Wt% (3) 0.60 wt% &lt; Si ^ 2.0 wt% ㈣ ^ = is added as a deoxidizing element, so It is usually contained in steel. In the current month, I actively added Si to assist cutting; the improved addition obtained due to the addition not only occurred in the low hardness (about ^^ 95) state after annealing, but also occurred. In the high hardness state after tempering (HRC61 or greater), the addition of meaning also helps to improve the tempering hardness of the south temperature. In order to obtain this effect, it is necessary to add si in a content exceeding 0.6, even after 200536945 虿Si, but the effect has reached saturation. Therefore, the Si content is preferably set to 2.0 wt% or less; and the silicon content is 065 wt% or more and ι 8 wt% or less, if it is 0. , 7wt% or more and ι · 5wt% or less are better. (4) 0.10 wt% ^ Mn ^ 1.0 wt%, _ has an increased hardenability to The effect of improving the hardness and strength, which reacts with the high-speed cutting element S, thereby forming an inclusion compound (inciusi0n) to effectively improve the cutting properties. In order to obtain this effect, the required Mn addition amount is 0.11. wt% or more; when Mn is added in excess, the hot workability is destroyed, so the Mn content is preferably 10 plus% or less. (5) 0.03 wt% ^ S ^ 0.2 wt% S is a high speed Cutting elements, which will bond with ^ to form inclusion complexes to improve workability. The improved workability obtained by adding S not only occurs in the low hardness (about HRB 95) state after annealing, but also occurs in quenching or High hardness state after tempering (taken 61 or greater). In order to obtain this effect, 0 03 plus% or more of s must be added. When s is added in excess, the check impact in the material block ( Chaipy impact) value will be greatly attenuated '. Therefore, the Si content is best set at 0.2 or lower. (6) 1.25 wt% &lt; Mo + 0.5 W &lt; 3.0 wt%

Mo及W係形成碳化物，以增加在45(rc或更高溫度下進行回 火f二次硬化量。雖然Mo及W具有相同效果，但為具有與Mo 相4之效果，需要雙倍w量，故M〇及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HRC61或更大之硬度，M〇當量須 大於1·25 wt/〇，然而，當M〇當量過大時，熱加工性、勃性、及 加工性即顯惡化，因此，Mo當量最好小於3.0 wt%。 (7)0.05 wt%$V$ ΐ·〇 埘〇/0 V，形成穩定碳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。為獲得這些效果，必須添 加0.05 wt%或更多含量之v，當v含量過高時，因碳化物量的增 200536945 加將令加工性及熱加工性降低，因此，v含量最好設定於1〇加％ 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 更多元素，各元素之組成範圍及限制理由將說明如下。 (8) 0.005 wt%SSe$〇.l〇 加〇/0 (9) 0.005 wt%STe$〇.l〇 wt〇/〇 (10) 0.0002 wt%$Ca$〇.〇l〇 加〇/0 (11) 0,005 wt%^Pb^〇.i〇 wt〇/〇 (12) 0.005 wt%^Bi^〇.i〇wt〇/0 吾人可添加Se，Te，Ca，Pb及/或Bi以提升加工性，加入這些 元素且添加Si並不會抑制加工性上之改良。 二 /、，Mn-硫化物中，Se及Te可作為s之替代元素；Ca可藉由 形成氧化物或溶解於Μη-硫化物中，以於加工時在切削工具表 ^形成保護膜而提升加卫性；又，加頌產生之祕令低溶點材 料之Pb及Bi縣，以期於切削工具與切角間產生潤滑效果 提升加工性。 •為獲得此種^果’上述元素之添加量必須大於或等於其下限 值；因過度添加這些元素將破壞鋼材之機械特性，故其添加 好設定在小於或等於上述上限。 (13) 0.01 wt%^Cu^2.0 wt% (14) 0.01 wt%^Ni^2.0 wt% (15) 0.20 wt%^Co^ l.o ^〇/0 (16) 0.0003 〇·〇ι〇 wt〇/0 +曰Nl，C〇及B係溶解於基質中以有效地提升可硬化性；Ni 亦具有猎由減少衝擊轉移（impaettransitiGn)溫度以增蝴性 避倾壞锻接性之效果。在冷模中，依高抗拉“ 加工發熱（WGridng-heating)而使模具溫 度局j升一㈣。Co具有藉由此—溫度提相增進高溫強 避免核具發生永久變形的效果。為獲槪些效果，這些元素的添 200536945 加^最好設定於大於或等於上述下限值，·因過度添加這些 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^〇.〇3〇 wt°/〇 (18) 0.0050 wt%^N^0.050 wt% (19) 0.001 wt%^A1^0.1〇 wt% (20) 0.0002 wt%^0.010 wt〇/〇 /、^N，0係無可避免地包含於鋼材中，p隔離於顆粒邊界中， 形成氧化物，且N形成氮化物。在鋼材中，Ai與〇或N _ 形成氧化物或氮化物，這些元素可藉由減少其添加量 性、。為獲得此-效果，這些元素的添加量最好設定於小 = 上述上限值；最好P佔〇·〇2〇#/〇或更少^佔〇 〇3〇wt 小； A1佔〇.〇5〇wt%或更少，〇佔〇 〇5〇wt%或更少。 〆^、 曰A1之氧化物或氮化物有助於防止顆粒粗化，是故若這些 少反之即變粗而破壞鋼材韌性。為減S於需 ^小於值時，提升勤性的效果亦達飽和，“，這】 素的含量最好設定在大於或等於上述下限值。 一 (21) 0.010 wt%^Nb^〇.l〇 wt% i (22) 0.005 wt%^Ta^〇.l〇 wt〇/〇 (23) 0.005 wt%^Ti^〇.l〇 ^〇/0 (24) 0.005 wt%^Zr^〇.l〇 wt% (25) 0.005 wt%^ Mg ^0. l〇 wt〇/〇 (26) 0.005 wt%^REM^0. l〇 wt% 1^\^?7^%及刪每一種均可有效地提升勃性，其中 性·，Γμ 賴細魏化物且藉__細化而提升^ 為貝i藉由減少基f中之氧含量而有效地提物性。 处下限值；當添加量秋時，將會破壞鋼材之嫌及锻接,=，' 11 200536945 故其添加量最好設定在小於或等於上述上限值。 及回㈣具有上述組成之材料加以淬火 火而仵。當回火溫度低時，在淬火時導入之殘餘岸力之釋放 =5:壞=加工性，因此，回火溫度最好;定在ί於 又I二體而έ，乘鬲硬度大於或等KHRC61)〇 勒性i==r〇rrtenite)之粒徑會影響勒性。為獲得具有高 :it ^ 較小之¥_田鐵之粒徑；然而， •田粒仫過小時，效果即降至最低，如此勢必增加成本，故夢沃斯 徑最好奴至顆粒尺寸Gq為大於‘於=以== ί係‘之粒徑尺寸， ：：^0^ -c 瞻徑粗化。 田口人在此/皿度靶圍進仃净火時，即可避免粒 =:5嫩之包合物估輯蚊之包合物，么= LT/λ ； 取大長度為20 μιη或更小之Α型包合物最好佔整體Α型包合物 12 200536945 30%比率。 為形成此一 A型包合物，Mn之添加量必須 旦 最少必須大於或等於S含量(Wt%)二73/·因五n 人亦需要]Vtn來促進可硬化性，故μ 口 ’口口Mo and W form carbides to increase the amount of secondary hardening at 45 ° C or higher. Although Mo and W have the same effect, in order to have the same effect as Mo phase 4, double w Therefore, the content of Mo and W is adjusted by the Mo equivalent described in Mo + 0.5 W. After quenching and tempering, in order to obtain hardness HRC61 or greater, the Mo equivalent must be greater than 1.25 wt / 〇 However, when the Mo equivalent is too large, the hot workability, toughness, and processability are significantly deteriorated, so the Mo equivalent is preferably less than 3.0 wt%. (7) 0.05 wt% $ V $ ΐ · 〇 埘 〇 / 0 V, forming stable carbides to effectively prevent particle coarsening, which also helps to improve wear resistance and hardness by forming carbides. To obtain these effects, 0.05 wt% or more of v must be added When the v content is too high, the increase in the amount of carbides 200536945 will reduce the workability and hot workability. Therefore, the v content is preferably set to 10% or less. In addition to the above elements, the cold work of the present invention Tool steel may further include one or more of the following elements, and the composition range and reasons for limitation of each element will be explained below. (8) 0.005 wt% SSe $ 〇.10 added 0/0 (9) 0.005 wt% STe $ 〇.10 wt〇 / 〇 (10) 0.0002 wt% $ Ca $ 〇.〇10 added 0/0 (11) 0,005 wt% ^ Pb ^ 〇.i〇wt〇 / 〇 (12) 0.005 wt% ^ Bi ^ 〇.i〇wt〇 / 0 We can add Se, Te, Ca, Pb and / or Bi to improve processability, The addition of these elements and the addition of Si will not inhibit the improvement in processability. Ⅱ ,, Mn-sulfide, Se and Te can be used as alternative elements of s; Ca can be formed by oxide or dissolved in Mn-sulfide In order to form a protective film on the cutting tool table during processing to enhance the security; In addition, the secrets of the low melting point materials Pb and Bi counted by Kason, in order to produce a lubricating effect between the cutting tool and the cutting angle to improve processing In order to obtain this kind of fruit, the above-mentioned elements must be added in an amount greater than or equal to the lower limit; as excessive addition of these elements will destroy the mechanical properties of the steel, the addition is set to be less than or equal to the upper limit. (13 ) 0.01 wt% ^ Cu ^ 2.0 wt% (14) 0.01 wt% ^ Ni ^ 2.0 wt% (15) 0.20 wt% ^ Co ^ lo ^ 〇 / 0 (16) 0.0003 〇 · 〇ι〇wt〇 / 0 + Nl, Co and B are dissolved in the matrix to effectively Improve the hardenability; Ni also has the effect of reducing the impact transfer temperature (impaettransitiGn) temperature to increase the resistance to avoid the collapse of the forgeability. In the cold mold, according to the high tensile "WGridng-heating" to make the mold The temperature bureau j rose a moment. Co has the effect of increasing the high temperature strength by this temperature increase phase to avoid permanent deformation of the rig. In order to obtain some effects, the addition of these elements 200536945 plus ^ is preferably set to be greater than or equal to the above-mentioned lower limit, · Because the mechanical properties of these steels are excessively added, the amount of addition is preferably set to less than or equal to the above-mentioned upper limit value. (17) 0.001 wt% ^ P ^ 0.30wt ° / 〇 (18) 0.0050 wt% ^ N ^ 0.050 wt% (19) 0.001 wt% ^ A1 ^ 0.1〇wt% (20) 0.0002 wt% ^ 0.010 wt ///, ^ N, 0 is inevitably contained in the steel, p is isolated in the grain boundary, forms an oxide, and N forms a nitride. In steel, Ai forms oxides or nitrides with 0 or N _, and these elements can be added by reducing the amount of addition. In order to obtain this effect, the addition amount of these elements is preferably set to be small = the above-mentioned upper limit value; it is preferable that P accounts for 〇.〇2〇 # / 〇 or less ^ accounts for 〇03〇wt small; A1 accounts for 〇. 05% by weight or less, and 0% by 05% by weight or less. 〆 ^, the oxide or nitride of A1 helps prevent the coarsening of the particles, so if these are less, they will become coarse and damage the toughness of the steel. In order to reduce the value of S when the required value is less than the value, the effect of improving the communality is also saturated. "The content of the element is preferably set to be greater than or equal to the above lower limit. One (21) 0.010 wt% ^ Nb ^ 〇. 10 wt% i (22) 0.005 wt% ^ Ta ^ 0.10wt〇 / 〇 (23) 0.005 wt% ^ Ti ^ 〇.l〇 ^ 〇 / 0 (24) 0.005 wt% ^ Zr ^ 〇. l〇wt% (25) 0.005 wt% ^ Mg ^ 0. l〇wt〇 / 〇 (26) 0.005 wt% ^ REM ^ 0. l〇wt% 1 ^ \ ^? 7 ^% and delete each Effectively enhances the robustness, its neutrality, Γμ depends on the fine Wei compound and is improved by __ refinement ^ is the effective improvement of physical properties by reducing the oxygen content in the base f. Lower limit value; when the amount of addition In autumn, steel materials will be destroyed and forging, =, '11 200536945 Therefore, the added amount is preferably set to less than or equal to the above upper limit value. And the materials with the above composition are quenched and quenched. When returned When the fire temperature is low, the release of the residual shore force introduced during the quenching = 5: bad = processability, so the tempering temperature is best; set at Γ and I, and the hardness is greater than or equal to KHRC61) 〇lerability i == r〇rrtenite) particle size will affect the lerability. In order to obtain a high: it ^ smaller ¥ _ Tiantie's particle size; however, • If the grain size is too small, the effect will be reduced to a minimum. This will inevitably increase the cost. Therefore, the Dreamworth diameter is best to be controlled until the particle size Gq is greater than '于 = 以 == ί 系The size of the particle size, ：: ^ 0 ^ -c The path diameter is roughened. When the Taguchi people enter the net fire around the target, the particle can be avoided =: 5 Compound = LT / λ; Take A-type clathrates with a large length of 20 μm or less, preferably 30% of the total A-type clathrate 12 200536945. In order to form this A-type clathrate, Mn The added amount must be at least greater than or equal to the S content (Wt%). 73 / · Because five people also need] Vtn to promote hardenability, so μ mouth 'mouth mouth

含量（Wt%)之_含了量更=)故施之添加垔通常多於適合S 包合物意指利請_中所述之= &gt; 60 X為削性質及耐衝擊性之冷作工具鋼， ”體而吕取好小於或等於0.05%;厂d(B+C) 60 X _ G0555 ;物=功率光學顯微鏡、6〇〇F〇V (視角）觀察下之包 有古ΪΪ將月之冷作工具鋼的效果。因為結晶碳化物具 ^ ί而Ui之耐磨耗性可藉由分散大量結晶碳化物來 : ’，，、、'=大里、、、口日日碳化物不僅會破壞加工性，亦會使線切割 粒又二常C斷，晶碳化物易於成為斷裂之始點，因其顆 _ 性^方面，結晶碳化物過少將使得硬度降低、 的旦之ί作t具鋼中’因在最適化l值時結晶化碳化物 工ϊ的線斷ί門顳可ί:加工性，且亦可減少例如線切割放電加 者’因成為斷裂之始點之粗化結晶碳化物 顆粒亦變得微細，故可達到高韋刃性。 I- 述適當泮火溫度下基質中之殘餘Cr含量，且必 且;；有助=====Si為-，^ 次硬化硬度。仰火/皿度以上之硬度；又，M。當量會影響二 本电明之冷作工具鋼可麵大於或等^HRC61之硬度，其為 13 200536945 ί作其他因為除了令κ#最適化 Α去及以〇當量亦加以最適化。 應力可充分回火，在淬火時於材料中所產生之殘餘 ^, 因此，除了具備優異加工性之外，即使在淤 電口工或線i謂放電加工時，亦可防止鋼材斷裂或毀損。The content (Wt%) _ the content is more =) Therefore, the addition of 垔 is usually more than suitable for S inclusion compound means that the _ mentioned in the description = &gt; 60 X is cold work with cutting properties and impact resistance Tool steel, the volume is less than or equal to 0.05%; the factory d (B + C) 60 X _ G0555; the object = power optical microscope, 600F (V) The effect of cold working tool steel. Because crystalline carbides have ^ ί and Ui's wear resistance can be dispersed by a large amount of crystalline carbides: ',,,,' = Dali ,,, and daily carbide It will destroy the workability, and it will also make the wire-cut grains break frequently, and the crystalline carbides are easy to be the starting point of fracture. Because of its grain size, too little crystalline carbides will reduce the hardness. In the steel, 'because the wire break of the carbide carbide is crystallized when the value of l is optimized, the processability can be reduced, and for example, wire cutting discharges can be reduced, and coarsening crystals which become the starting point of fracture are reduced. The carbide particles also become fine, so it can achieve high cutting edge properties. I- The residual Cr content in the matrix at the appropriate annealing temperature, and must ;; help ===== Si is- , ^ Secondary hardening hardness. Hardness above the fire / plate degree; and, M. Equivalent will affect the hardness of the two electric tools cold work tool steel surface can be greater than or equal to ^ HRC61, which is 13 200536945. κ # is optimized by A and optimized by 0 equivalents. The stress can be fully tempered, and the residue generated in the material during quenching ^, so in addition to having excellent processability, Line i means that the steel can also be prevented from being broken or damaged during electrical discharge machining.

又’材料易於在南速範圍（高轉速）加工時锻接至切削面， 2，工具極㈣鍛接部分之反覆形成及分離而持續磨韻。在本 叙月之冷作工具鋼中，因Si之添加量為大於或等於0·ό wt%，不 易^生鍛接情形，及可抑制工具的磨蝕；因此，冷作工具鋼可 有較習知高速切削鋼為高之可加工性。 y'The material is easy to be forged to the cutting surface during machining in the south speed range (high speed). 2. The repeated formation and separation of the forged part of the tool pole and the continuous grinding of the rhyme. In the cold-working tool steel of this month, because the amount of Si added is greater than or equal to 0 · ό wt%, it is not easy to forge the forging situation, and it can suppress the tool's abrasion; therefore, the cold-working tool steel can be more familiar High-speed cutting steel has high machinability. y '

MM 將具有表1 (範例1至20及比較範例1至i〇)所示各元素組 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禱塊 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8g〇°C逐漸地冷卻方形棒來施行球化處理。 14 200536945 表1 妹 i j 〇 g 1? 80 寸 GO o . ?! •一丨 £0 卜^ Ο If £ Τβ=0.083 C〇=0.43 I Se=0.031, B=0,0007 I j I I i J 5 § I i i I |Mg=0.084 g c&gt; Λ g If &gt;2 g 5 i 1 1XL &lt;g&gt; § I ! I 1 j • I L值 8.3751 7.51 Γ i0.525 Z0.98 to CM &lt;6 1T^ U； Ln JM·. 〇% 卜 cd b cd \Ύ^ 19.645 19.585 16.71 % 卜 rf s Ol CO V— I20.395 CD s 20.625 17.92 U&gt; K UD Oi οι &lt;d U) CO &lt;〇 17.855 17.015 33.23S 131.05 ί|28.04£ 124.95 &gt;|23.30i Μ r-* ig • &lt;D XO ).678； 191飞 11 寸 c4 ICO GO 〇&gt; CO γΜ &lt;〇 Ol !. 1.136 1.96BI 1.992 t— o 12· 332 &lt;〇 c4 &lt;α oo 5f = g CO (Ο 5： οί CO CM CM· ▼— ri CM 3.13 3.39E &gt;3.295 v· trr |0.33( Ο 1 I 1 I r |l Γ- I !l 1 1 i 1 \) 1 I I I f 8 s. S O o' |C〇 &amp; 丨V- 5 o s O- 1 !cO g d 0.0084 i O CO 8 O 〇&gt; o 1 I I 0. 0001 CO !§ O 0.031 I |0.000E v^l 1寸 o o 1 0.005 ο e. in o 〇* 0.011 0.009 &quot;oo &lt;M r—· Τ Ο 0.034 0.021 1 1 I 2： i| I 1 I i t I I I 1 1 1 I I ! § a f O S O o !·0 CO o Q 0.003 I I o T ! § ! 0.169 I (0.034 $ 1 I 7 I 1 1 1 1 7 1 1 I I I J S O s o £ o CO CM CD s o o 0.01 0.02 O 0.24 0.27 |0.33 &gt; 〇 0.23 0.19 0.17 ▼— a 0.11 0.09 s 0.051 〇J2 s o. 0.33 s 〇_ o &amp; 〇* 0© r- 〇 I 1 !i co&quot; \Xi o 1 CO o ΣΖ. CO UO V* ! ^rr \\t 35 i0.09 I Ί=Γ ΪΟ CO # 1 7 0.46 3)0.19 ο 3 I I I ).06 1 I 1 3..11 1 D. 31 I I f 〇 uT CM ΚΓ CO ΤΓ— co~ CO s t— 〇r in ο CO % CO TT— Uli of CO csi MU in oo pi 2.93 oi w ?i cJ v-· 00 5. 11 11 11 11 11 艺 CM 0.34 CO o 0.9E 1.95 co r£ 2.0, c&gt;i 8.31 «Γ LO &lt;d 6.94 6.23； 6.01 12.31 CO CO -r— 二 10. 84 8. 83 ώ LO 丨卜 &lt;d LO 泛 cd το GO ^Γ &lt;〇 &lt;d 6.21 &lt;d aT CO 6.33 oa Γ： r ,7.34 cd 6.11 oo 〇&gt; u&gt; Is !r^ £ 0.13 Ο I 1 Ϊ I 1 0.02 1 CM 1 丨1 I I I 卜 ：| 1 I 「.〆 I ! ι ! 1 0.21 0.81 S O 0.23 σ&gt; IQ s o a ΓΓ I I I 丨I ΓΓ i 1 ~ |l I 17 IT D. 09 c&gt; CO o g r-* 〇 〇. o.u 0. 33 E Ι I 10. Oi J I CO I C&gt;! 〇. CO 1 co (0 D. 065 0.085 0.093 0.134 0.153 0.194 0.034 0.043 0.053 0.083 0.075 0.087 g O S °. o ού &lt;〇 o o oo 呂 o c〇 5 0.015 0.041 IS 〇 !〇 0.011 0.04E 0.072 § o 0·00, iO.OO； o o o ο csl o TO. 021 i0.013] I 1 1 a O 5 0.021 JO. 011 I δ Ϊ 1 ϊο Ο. 1 I I 丨 ；1 1 1 ι— I I I I 1 I !· ! I I 8 o S £ —J LO m FT CO «Γ CO CO CO 〇&gt; I ca&quot; 〇% V121 to ca 〇 〇3! S O ίο LO 〇 a O 荔 o 0.41 0.53 0.44 a 〇 Μ P. 10.43 CO ir-*» s 〇 30.4f CD # 1q o CS| &lt;〇 ο οι CO 〇 CO Ο 5 o S ΪΛ CO o 泛 o CO «Ί 〇&gt; g- 2S-U CM CO S • ι —7— CO ^r·* S| 丨 S&gt; t— W LO CD 〇 S 〇. SI ol 〇&gt; 00 o s ΤΓ-· 〇 10. CO 〇_ o CM CO # s 〇 &lt;〇 s Q ri oo 昏 Ο LO 卜 o σ&gt; oe&gt; o s c5 CO GO CO 卜 &lt;〇 s ^- 〇 CO 〇 0. 83 S&quot; o. 0.66 VO o cT 00 .1 o L〇· 85 0.62 〇&gt; to 〇. CO 艺 o ο ί^: 辦丨 〇 o CM o o 〇 iX&gt; 〇. &lt;〇 o 卜 CO SL Oi —1—一 Y—- cO U) &lt;〇 T~ CO T&quot;~ i □ r 寸 Π Ί 、囑 1 1 — — — — — —- 1 - £ 省鑑缄參l 1 — __ -----— 一 各元素組成係以「重量百分率」（Μ%)來表示；κ值及1/值 亦同。 15 200536945 每一種產生之鋼材產品均受到加工性測試（端銑加工測試）、 線切割放電加工測試、硬度估計、查比衝擊測試、淬火後顆粒尺 寸Gq、以及包合物含量估計。 加工性測試（端銑加工測試）係施行至在球化退火狀態自鋼 材產品切割下來之一測試片。測試條件如下： 工具：燒結碳化物（cementedcarbide) Μ20 ( 0 32mm) 速率：200 m/min 饋入速率：0.15mm/rev 切削寬度：4.5 mm 切削高度：1.2 mm •切削油·無 工具壽命：在刀具侧腹部之最大磨耗量達0.3 mm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 50x 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馨成10 X 20 mm之方形狀；在施行放 鲁 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 20 X 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 试片之平均值做為衝擊值。 ' 顆粒尺寸Gq係根據JISG0551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 16 200536945 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結 果，L值與結晶碳化物量間之關係則顯示於圖1。 表2MM melted a steel material having the elements shown in Table 1 (Examples 1 to 20 and Comparative Examples 1 to i0) in a high-frequency vacuum furnace. The steel prayer block obtained by casting is hot forged to form a square bar of 35 X 55 mm; after hot forging, the square bar is gradually cooled from 8 g0 ° C at a cooling rate of 7 ^ / hr. Spheroidization. 14 200536945 Table 1 Girl ij 〇g 1? 80 inch GO o.?! • One 丨 £ 0 Bu ^ 〇 If £ Τβ = 0.083 C〇 = 0.43 I Se = 0.031, B = 0,0007 I j II i J 5 § I ii I | Mg = 0.084 g c &gt; Λ g If &gt; 2 g 5 i 1 1XL &lt; g &gt; § I! I 1 j • IL value 8.3751 7.51 Γ i0.525 Z0.98 to CM &lt; 6 1T ^ U; Ln JM ·. 〇% Bu cd b cd \ Ύ ^ 19.645 19.585 16.71% Bu r s Ol CO V— I20.395 CD s 20.625 17.92 U &gt; K UD Oi οι &lt; d U) CO &lt; 〇17.855 17.015 33.23S 131.05 ί | 28.04 £ 124.95 &gt; | 23.30i Μ r- * ig • &lt; D XO) .678; 191 to 11 inch c4 ICO GO 〇 &gt; CO γΜ &lt; 〇Ol!. 1.136 1.96BI 1.992 t— o 12 · 332 &lt; 〇c4 &lt; α oo 5f = g CO (Ο 5: οί CO CM CM · ▼ — ri CM 3.13 3.39E &gt; 3.295 v · trr | 0.33 (Ο 1 I 1 I r | l Γ- I! l 1 1 i 1 \) 1 III f 8 s. SO o '| C〇 &amp; 丨 V- 5 os O- 1! cO gd 0.0084 i O CO 8 O 〇 &gt; o 1 II 0 . 0001 CO! § O 0.031 I | 0.000E v ^ l 1 inch oo 1 0.005 ο e. In o 〇 * 0.011 0.009 &quot; oo &lt; M r— · Τ Ο 0.034 0.021 1 1 I 2: i | I 1 I it III 1 1 1 II! § af OSO o! · 0 CO o Q 0.003 II o T! §! 0.169 I (0.034 $ 1 I 7 I 1 1 1 1 7 1 1 IIIJSO so £ o CO CM CD soo 0.01 0.02 O 0.24 0.27 | 0.33 &gt; 〇0.23 0.19 0.17 ▼ — a 0.11 0.09 s 0.051 〇J2 s o. 0.33 s 〇_ o &amp; 〇 * 0 © r- 〇I 1! I co &quot; \ Xi o 1 CO o ΣZ. CO UO V *! ^ Rr \\ t 35 i0.09 I Ί = Γ ΪΟ CO # 1 7 0.46 3) 0.19 ο 3 III) .06 1 I 1 3..11 1 D. 31 II f 〇uT CM ΚΓ CO ΤΓ — Co ~ CO st— 〇r in ο CO% CO TT— Uli of CO csi MU in oo pi 2.93 oi w? I cJ v- · 00 5. 11 11 11 11 11 CM 0.34 CO o 0.9E 1.95 co r £ 2.0, c &gt; i 8.31 «Γ LO &lt; d 6.94 6.23; 6.01 12.31 CO CO -r— II 10. 84 8. 83 free LO 丨 b &lt; d LO pan cd το GO ^ Γ &lt; 〇 &lt; d 6.21 &lt; d aT CO 6.33 oa Γ: r, 7.34 cd 6.11 oo 〇 &gt; u &gt; Is! R ^ £ 0.13 〇 I 1 Ϊ I 1 0.02 1 CM 1 丨 1 III Bu: | 1 I 「.〆I! ι! 1 0.21 0.81 SO 0.23 σ &gt; IQ soa ΓΓ III 丨 I ΓΓ i 1 ~ | l I 17 IT D. 09 c &gt; CO og r- * 〇〇. ou 0. 33 E Ι I 10. Oi JI CO I C &gt;! 〇. CO 1 co (0 D. 065 0.085 0.093 0.134 0.153 0.194 0.034 0.043 0.053 0.083 0.075 0.087 g OS °. O ού &lt; 〇oo oo Luoc〇5 0.015 0.041 IS 〇! 〇0.011 0.04E 0.072 § o 0 · 00, iO.OO; ooo ο csl o TO. 021 i0.013] I 1 1 a O 5 0.021 JO. 011 I δ Ϊ 1 ϊο Ο. 1 II 丨; 1 1 1 ι— IIII 1 I! ·! II 8 o S £ —J LO m FT CO «Γ CO CO CO 〇 &gt; I ca &quot; 〇% V121 to ca 〇〇3! SO ίο LO 〇a O lyo 0.41 0.53 0.44 a 〇 Μ P. 10.43 CO ir- * »s 〇〇30.4f CD # 1q o CS | &lt; 〇ο οι CO 〇CO 〇 5 o S ΪΛ CO o oo CO« Ί 〇 &gt; g- 2S-U CM CO S • ι —7— CO ^ r · * S | 丨 S &gt; t— W LO CD 〇S 〇. SI ol 〇 &gt; 00 os ΤΓ- · 〇10. CO 〇_ o CM CO # s 〇 &lt; 〇s Q ri oo ΟΟ LO oo σ &gt; oe &gt; os c5 CO GO CO bu &lt; 〇s ^-〇CO 〇 0.83 S &quot; o. 0.66 VO o cT 00 .1 o L〇 · 85 0.62 〇 &gt; to 〇. CO 艺 o ο ^^: 丨 丨 〇o CM oo 〇iX &gt; 〇. &lt; 〇o Bu CO SL Oi —1— 一 Y—- cO U ) &lt; 〇T ~ CO T &quot; ~ i □ r inch Π Ί ， 嘱 1 1 — — — — — —- 1-£ 省 省 缄 参 l 1 — __ -----— An elemental composition is based on "Percent by weight" (M%); κ value and 1 / value are the same. 15 200536945 Each produced steel product is subject to workability test (end mill processing test), wire cutting electrical discharge machining test, hardness estimation, Charpy impact test, particle size Gq after quenching, and inclusion content estimation. The workability test (end mill machining test) is performed to one of the test pieces cut from the steel product in the spheroidizing annealing state. The test conditions are as follows: Tool: cementedcarbide M20 (0 32mm) Rate: 200 m / min Feed rate: 0.15mm / rev Cutting width: 4.5 mm Cutting height: 1.2 mm • Cutting oil and tool-less life: in Cutting distance estimation method when the maximum abrasion amount on the tool-side abdomen reaches 0.3 mm: A comparative estimation of the tool life of Tool Steel No. 1 as 100 is a wire cutting electrical discharge machining test based on the following steps. In short, a 30 X 50 x 200 mm test piece was cut from the nodular annealed steel, and the test piece was quenched and tempered under a predetermined condition; after drilling a 0 4 mm hole in the test piece, the test piece was used Wire-cut electrical discharge machining was squared into a 10 X 20 mm square shape; the number of cracks generated on the test piece was measured by 'making the test piece stand up to one day' after performing the Lu Dian machining. In terms of hardness, a 20 X 20 mm sheet test piece was cut from the nodular annealed steel, and the hardness after quenching and tempering was measured at a predetermined temperature; the tempering temperature at the specific temperature shown in Table 2 was measured. Numerical value (test hardness) and the maximum value (highest hardness) tempered at 100 to below. At room temperature, a Charpy impact test is performed on a 10R-notched Charpy impact test piece formed by self-spheroidizing annealed steel after quenching and tempering at a predetermined temperature, and the average of the three test pieces is used as the impact. value. 'The particle size Gq is measured according to the method described in JISG0551. The inclusion content of the A-type inclusion compound and the (B + C) -type inclusion compound is measured by the method described in JISG0555 16 200536945 (magnification of an optical microscope: 400, number of viewing angles: 60). Table 2 shows the results of the quenching temperature, tempering temperature, and various estimated tests. The relationship between the L value and the amount of crystalline carbides is shown in Figure 1. Table 2

f β CM g 〇 o o o o o o S ο ο ο s o O o o g o S 〇 O ο o CM 〇 〇 o o c? S O o s o o o o ε ο s o o’ s o o CO Y— o c? o o’ CO y— o’ o ο o S ο ο 蔡名 ,^4〇 CO CM 〇 LO 〇0 o o CO c\l r— CO ο» ο CO 1-· ▼—· o O) CM o a O |A o οο CO ο CO &lt;£i 〇 CO \£&gt; O’ LTD CO 〇 LA o 5 o CD CO o 穿 o &lt;〇 CM o C0 卜 ο g o s o o LA CM o CO CO o 1—· CO o s o o OJ o 〇 〇&gt; ο ο s o uy ο CO (Ο 1V i &lt;0 CO Ln ίΟ 卜 bd CO &lt;d CO xt 〇〇 CO uri 〇&gt; — a&gt; οο &lt;ό a&gt; CO LA 〇&gt; u&gt; ΓΟ i6 〇〇 &lt;d CM ai &lt;ό CO 卜： 卜· CO — CO ir&gt; (〇 io Oi 守 CO &lt;d LO Ο 卜 L0 f ^ CO CO LO CO eo CD CO CM CO LO CO CM CO LO CO irp CO CO CO CO CM CO 〇&gt; CO τ— 〇» CM 1 备 〇&gt; S? D 难 难 举 掣 举 雄 举 举 难 制 备 djoj yftl &gt; 则 ^8¾ \ —y Η 5 tn Oi CO § csl CO 00 οα CO &lt;s -r— (〇 GO »—· a CM ss CM S CM CO § CO a% CSi LO σ&gt; &amp; CO LO s CM 8 CM 8 CO C&gt;J CQ CO V·» i? -r~ 〇&gt; (Ο CO 00 LO &lt;〇 卜 ύ S C4 (Ο 'Τ—- C4 S 餐u 滅茔 CO s ▼—* oi &lt;〇 T— CO (0 05 15 V οί CO C4 oi &lt;〇 OI c^i &lt;〇 ύ CM 5 CM CO CO ύ CM 〇si co CM_ &lt;〇 'r—· C4 &lt;〇 5 CM C4 &lt;〇 〇&gt; &lt;〇 oo z cvi VO CM C4 &lt;〇 CO σ&gt; u&gt; ή CO LO 卜 &lt;d LO CO σ&gt; to csl σ&gt; ΙΟ 寸 00 u&gt; -K X GO c*i CO CO c〇 09 CO co ύ CM CM· «Ο »—· CO CO &lt;0 〇〇 c4 «〇 CO c6 CP CM ςνί ς〇 &lt;3i C〇 &lt;0 a&gt; t 卜 ΊΤ— CO csi CO 00 CO C0 CO CO CO T— cvi %〇 CO CO (0 CO oi lO CO to 卜 &lt;d U3 a% CO CO CO CP r- CO τέ :s o L〇 s L〇 o 穿 O 〇 iXi o o 穿 § ο o LT&gt; o s o LA o CM b〇 o 运 〇 s 〇 (0 另 寒 s o s o s ο un esl o U3 o 穿 o o 〇 uH ο S Ί s o u&gt; o o o ο τ— o 〇&gt; σ&gt; o s ▼— | r^· kO CO 〇〇 o a&gt; 1 ο s o ▼— LO CM 〇 CM o CO 〇 5 T~ u&gt; Τ Ο LX&gt; s o to 〇 S r— 卜 s o oo ο 〇} o s w CO o ir— s o Csl s ο co s o o o m | CO LO o Ύ— 卜 ο LA ^r- OO ο α&gt; ο S ο CM CO ΙΩ CO i τ* r— J J 革 17 200536945 如圖1所示，L值與結晶碳化物量之間存在一關係式，且當l 值超過21.0時，結晶碳化物量則超過4 0加％。在比較範例1及 6〜10中，每一範例之L值均極大，故結晶碳化物量多，因此，鋼 材之衝擊值低且力口工性差；特別是比較範例7及8，線切割放電力口 。工即導致線斷裂；在比較範例3, 9及1G中，_火溫度低於45〇 ^：，放電加工後便產生斷裂；再者，在比較範例2, 4及5中，其 最大硬度小於HRC 61，因合金元素施，M〇，及v並不在本發明 之範圍内；在比較範例6中，因&amp;值過大而無法達到充分二次硬 化，且最大硬度小於HRC61。 μ反田之’本發明鋼材（範例）1〜20每一種均具備大於或等於HRC =大硬料Κ值、L值及其他合金元素之每一元素量 高^4均已最適化，故其顯示出具有優異加工性及放電加工性之 wt%S 3 加量與加工性間之關係，其中當Si含量佔0.6 在於祕織所致之工 於上ΪΪ日實施例已詳細說明於上；然而，本發明絕非僅限 施例’在不偏離本發明之主旨下，本發明可作各= 不同作工具鋼可絲作為各種抑之冷賴具及各種 五、【圖式簡單說明】 值與結晶碳化物含4之間_係；以及 圖2顯不Si含量與加工性之間的關係。 【主要元件符號說明】 18f β CM g 〇oooooo S ο ο ο so O oogo S 〇O ο o CM 〇〇ooc? SO osoooo ε ο so o 'soo CO Y— oc? o o' CO y— o 'o ο o S ο ο Cai Ming, ^ 4〇CO CM 〇LO 〇0 oo CO c \ lr— CO ο »ο CO 1- · ▼ — · o O) CM oa O | A o οο CO ο CO &lt; £ i 〇CO \ £ &gt; O 'LTD CO 〇LA o 5 o CD CO o wear o &lt; 〇CM o C0 bu gosoo LA CM o CO CO o 1— · CO osoo OJ o 〇〇 &gt; ο ο so uy ο CO (Ο 1V i &lt; 0 CO Ln ίΟ bd CO &lt; d CO xt 〇〇CO uri 〇 &gt; — a &gt; οο &lt; ό a &gt; CO LA 〇 &gt; u &gt; ΓΟ i6 〇〇 &lt; d CM ai &lt; ό CO Bu: Bu CO — CO ir &gt; (〇io Oi Shou CO &lt; d LO Ο Bu L0 f ^ CO CO LO CO eo CD CO CM CO LO CO CM CO LO CO irp CO CO CO CO CM CO 〇 &gt; CO τ— 〇 »CM 1 Preparation 〇 &gt; S? D is difficult to make a masterpiece and difficult to prepare djoj yftl &gt; then ^ 8¾ \ —y Η 5 tn Oi CO § csl CO 00 οα CO &lt; s- r— (〇GO »— · a CM ss CM S CM CO § CO a% CSi LO σ &gt; &amp; CO LO s CM 8 CM 8 CO C &gt; J CQ CO V · »i? -R ~ 〇 &gt; (Ο CO 00 LO &lt; 〇 卜 ύ S C4 (〇 'Τ—- C4 S 食 u 灭 COCO s ▼ — * oi &lt; 〇T— CO (0 05 15 V οί CO C4 oi &lt; 〇OI c ^ i &lt; 〇 CM 5 CM CO CO ύ CM 〇si co CM_ &lt; 〇'r— · C4 &lt; 〇5 CM C4 &lt; 〇〇 &gt; &lt; 〇oo z cvi VO CM C4 &lt; 〇CO σ &gt; u &gt; price CO LO &lt; d LO CO σ &gt; to csl σ &gt; 10 inch 00 u &gt;-- KX GO c * i CO CO c〇09 CO co ύ CM CM · «Ο» — · CO CO &lt; 0 〇〇c4 «〇CO c6 CP CM ςν ς 〇 &lt; 3i C〇 &lt; 0 a &gt; t ΊΤ— CO csi CO 00 CO C0 CO CO CO T— cvi% 〇CO CO (0 CO oi lO CO to & d U3 a% CO CO CO CP r- CO τέ: so L〇s L〇o wear O 〇iXi oo wear§ ο o LT &gt; oso LA o CM b〇o 〇s 〇 (0 Another cold sosos ο un esl o U3 o wear oo 〇uH ο S Ί so u &gt; ooo ο τ— o 〇 &gt; σ &gt; os ▼ — | r ^ · kO CO 〇〇o a &gt; 1 ο so ▼ — LO CM 〇CM o CO 〇5 T ~ u &gt; Τ Ο LX &gt; so to 〇S r— bu so oo ο 〇} osw C O o ir— so Csl s ο co sooom | CO LO o Ύ— bu ο LA ^ r- OO ο α &gt; ο S ο CM CO ΙΩ CO i τ * r— JJ Leather 17 200536945 As shown in Figure 1, L value A relationship exists with the amount of crystalline carbides, and when the value of l exceeds 21.0, the amount of crystalline carbides exceeds 40 plus%. In Comparative Examples 1 and 6 to 10, the L value of each example is extremely large, so the amount of crystalline carbides is large. Therefore, the impact value of the steel is low and the workability is poor; especially Comparative Examples 7 and 8, the wire cutting discharge force mouth. In the comparative examples 3, 9 and 1G, when the fire temperature is lower than 45 °: the fracture occurs after electrical discharge machining; furthermore, in the comparative examples 2, 4 and 5, the maximum hardness is less than For HRC 61, Mo and V are not within the scope of the present invention due to alloying elements; in Comparative Example 6, the &amp; value is too large to achieve sufficient secondary hardening, and the maximum hardness is less than HRC61. μ's anti-'steel steel of the present invention (examples) 1 to 20 each have a HRC = greater than hard material K value, L value and other alloy elements each high ^ 4 has been optimized, so its display The relationship between the addition of wt% S 3 with excellent processability and electrical discharge processability and processability, in which when the Si content accounts for 0.6 due to the weaving process, the examples have been explained on the previous day; however, The present invention is by no means limited to the examples. 'Without departing from the gist of the present invention, the present invention can be made different = different tool steel can be used as a variety of cold rigs and various five, [simple description of the figure] value and crystal The carbide contains between 4 series; and Figure 2 shows the relationship between Si content and processability. [Description of Symbols of Main Components] 18

Claims (1)

200536945 申請專利範圍： 1· 一種冷作工具鋼，包含： 0.4 $K 值 ^2·6 ( K 值=Qr (wt%) - 6.8 C (wtV) v 15.5$L 值$2ΐ·〇 (L 值=〇&lt;(wt〇/〇) + 15 ’ 0.60 wt%&lt;Si^2.0 wt% ； W/〇))， 0.10 wt%^Mn^ l.o wt% ; 0.03 wt% &lt; S ^ 0.2 wt% ； 1.25 wt%&lt;Mo + 0.5 W&lt;3.0 wt% ； 〇.〇5wt%$V$l.〇wt%;以及200536945 Patent application scope: 1. A cold work tool steel, including: 0.4 $ K value ^ 2 · 6 (K value = Qr (wt%)-6.8 C (wtV) v 15.5 $ L value $ 2ΐ · 〇 (L value = 〇 &lt; (wt〇 / 〇) + 15 '0.60 wt% &lt; Si ^ 2.0 wt%; W / 〇)), 0.10 wt% ^ Mn ^ lo wt%; 0.03 wt% &lt; S ^ 0.2 wt% 1.25 wt% &lt; Mo + 0.5 W &lt; 3.0 wt%; 〇.05wt% $ V $ l.〇wt%; and 剩餘部分Fe與無可避免之雜質； 其中藉由淬火後在45〇〇C或更高溫度下回火 為HRC 61或更大值。 π件之取大硬度 2·如申請專利範圍第1項之冷作工具鋼，更包含一哎更多選 擇自下列條件之元素： / 0.005 wt%^Se^0.10 wt% ； 0.005 wt%^Te^0.10 wt% ； 0.0002 wt%^Ca^0.010 wt% ； 0.005 wt%$Pb$0.10wt% ;以及 0.005 0.10 wt%。 3·如申請專利範圍第i項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.01 wt%^Cu^2.0 wt% ； 0-01 wt%^Ni^2.0wt% ； 〇.20wt%$Co$1.0wt%;以及 0.0003 wt%SB$0.010wt%。 4.如申請專利範圍第2項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： / 0.01 wt%^Cu^2.0 wt% ； 0.01 wt%^Ni^2.0 wt% ； 19 200536945 OL/c^Co^l.Owt% ;以及 0.0003 wt%$B$0 010 _〇/〇。 5·如申請專利範圍第1項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： 0.0010 Wt%^p^0.030 wt% ； 0.0050 wt%^N^0.050 wt% ； (XOOlOwtG/o^AlgO.lOwt% ;以及 0.0002 wt%$〇$〇 oio 加％。 6·如申請專利範圍第3項之冷作工具鋼，更包含一或更多選 • 擇自下列條件之元素： 0.0010 wt%^P^0.030 wt% ； 0.0050 wt%0.050 wt% ； 0.0010 wt%$Al$0.10 wt% ;以及 0·0002 wt%$0$〇.〇l〇 wt0/〇 〇 7·如申請專利範圍第4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%^p^0.030wt% ； 0.0050 wt%0.050 wt% ； • 0.0010 wt%$Al$0.10 wt% ;以及 0·0002 wto/〇SOS0.010wt% 〇 8·如申請專利範圍第6項之冷作工具鋼，更包含一或更多選 擇自下列條件之元素： / 0.010 wt%^Nb^0.10 wt% ; 0.005 wt%^Ta^0-10 wt% ； 0-005 wt%^Ti^0.10 wt% ； 0.005 wt%^Zr^0.10 wt% ； 0.005 wt%SMg^〇.l〇wt% ;以及 0·005 wt%$REMS0.10 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 20 200536945 擇自下列條件之元素： 0.010 wt%^Nb^0.10wt% ； 0.005 wt%^Ta^0.10 wt% ； 0.005 wt%^Ti^0.10 wt% ； 0.005 wt%^Zr^0.10 wt% ； 0.005 wt%$Mg^0.10wt% ;以及 0.005 wt%$REM$0.10 wt0/〇 〇The remaining Fe and unavoidable impurities; among them, HRC 61 or greater by tempering at 4500C or higher after quenching. Large hardness of π pieces2. For example, the cold work tool steel in item 1 of the scope of patent application, it also contains one more element selected from the following conditions: / 0.005 wt% ^ Se ^ 0.10 wt%; 0.005 wt% ^ Te ^ 0.10 wt%; 0.0002 wt% ^ Ca ^ 0.010 wt%; 0.005 wt% $ Pb $ 0.10wt%; and 0.005 0.10 wt%. 3. If the cold work tool steel in item i of the patent application scope, further contains one or more elements selected from the following conditions: 0.01 wt% ^ Cu ^ 2.0 wt%; 0-01 wt% ^ Ni ^ 2.0wt%; 〇.20wt% $ Co $ 1.0wt%; and 0.0003wt% SB $ 0.010wt%. 4. If the cold-working tool steel of item 2 of the patent application scope, further contains one or more elements selected from the following conditions: / 0.01 wt% ^ Cu ^ 2.0 wt%; 0.01 wt% ^ Ni ^ 2.0 wt%; 19 200536945 OL / c ^ Co ^ l.Owt%; and 0.0003 wt% $ B $ 0 010 〇 / 〇. 5. If the cold work tool steel in item 1 of the patent application scope, it further contains one or more elements selected from the following conditions: 0.0010 Wt% ^ p ^ 0.030 wt%; 0.0050 wt% ^ N ^ 0.050 wt%; (XOOlOwtG /o^AlgO.lOwt%; and 0.0002 wt% $ 〇 $ 〇oio plus%. 6. If the cold-working tool steel in the scope of the patent application No. 3, contains one or more elements selected from the following conditions: 0.0010 wt% ^ P ^ 0.030 wt%; 0.0050 wt% 0.050 wt%; 0.0010 wt% $ Al $ 0.10 wt%; and 0 · 0002 wt% $ 0.00l0wt0 / 〇〇7. 4 cold work tool steels, further comprising one or more elements selected from the following conditions: / 0.0010 wt% ^ p ^ 0.030wt%; 0.0050 wt% 0.050 wt%; • 0.0010 wt% $ Al $ 0.10 wt%; and 0 · 0002 wto / 〇SOS0.010wt% 〇8 · If the cold-working tool steel of item 6 of the patent application scope, further contains one or more elements selected from the following conditions: / 0.010 wt% ^ Nb ^ 0.10 wt%; 0.005 wt% ^ Ta ^ 0-10 wt%; 0-005 wt% ^ Ti ^ 0.10 wt%; 0.005 wt% ^ Zr ^ 0.10 wt%; 0.005 wt% SMg ^ 0.11 wt%; and 0.005 wt% $ REMS0.10 wt% 9 · If the scope of patent application Cold work tool steel of 7 items, including one or more 20 200536945 elements selected from the following conditions: 0.010 wt% ^ Nb ^ 0.10wt%; 0.005 wt% ^ Ta ^ 0.10 wt%; 0.005 wt% ^ Ti ^ 0.10 wt%; 0.005 wt% ^ Zr ^ 0.10 wt%; 0.005 wt% $ Mg ^ 0.10 wt%; and 0.005 wt% $ REM $ 0.10 wt0 / 〇〇 10·如申請專利範圍第1項之冷作工具鋼，其具有010〇/〇彡’ 60 X 400^1.50%，其中「dA60 X 400」為根據JISG0555中戶斤述 之方法進行量測之包合物含量。 η·如申請專利範圍第2項之冷作工具鋼，其具有〇·1〇〇/0$Μ 60 X 40〇$ι·5〇%，其中「dA60 X 400」為根據 JISG0555 中所述 之方法進行量測之包合物含量。 12.如申請專利範圍第3項之冷作工具鋼，其具有〇·ι〇〇/0$(ΐΑ 60 X 40〇$ι.5〇〇/0,其中「dA60 X 400」為根據 JISG0555 中所述 之方法進行量測之包合物含量。 •如申請專利範圍第5項之冷作工具鋼，其具有〇1〇0/〇SdA 60 j 4〇〇$15〇%，其中「dA6〇 χ 4〇〇」為根據 jisg〇555 中所述 之方法進行量測之包合物含量。 Μ 1如申請專利範圍第6項之冷作工具鋼，其具有0.10〇/o^dA 之^本、^L50%’其中「dA60 x 400」為根據JISG0555中所述 ^万法進行量測之包合物含量。 60 X 巾*專利ί圍第7項之冷作工具鋼，其具有謂％^必 X 4〇0 J ^«JIS 00555 之方法進行制之包合物含量。x _」為喊nsGG555中所述 令申响專利範圍第1項之冷作工具鋼，可藉由在大於或等 21 200536945 於950C及小於或等於l〇8(TC之溫度下淬火，且3.〇$Gq$8.〇來 獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺寸，其係根 G0551中所述之方法進行測量。 18·如申請專利範圍第2項之冷作工具鋼，可藉由在大於戋 於950°C及小於或等於1080它之溫度下淬火，且3 〇gGq$8 〇來 獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺寸，其係根 G0551中所述之方法進行測量。 19·如申請專利範圍第3項之冷作工具鋼，可藉由在大於 於950°C及小於或等於l〇8〇°C之溫度下淬火，且3x)gGq$8 〇來10. If the cold work tool steel of item 1 of the patent application scope has 010 / 〇 彡 '60 X 400 ^ 1.50%, of which "dA60 X 400" is a package measured according to the method described in JISG0555组合 物 量。 Content. η · The cold-working tool steel according to item 2 of the patent application scope, which has a value of 0.100 / 0 $ M 60 X 40.00 $ 50%, in which "dA60 X 400" is described in accordance with JISG0555 Method The content of inclusion compound was measured. 12. The cold work tool steel according to item 3 of the patent application scope, which has 〇〇〇〇 / 0 $ (ΐΑ60 X 40〇 $ ι.500 / 0, where "dA60 X 400" is in accordance with JISG0555 The content of the clathrate is measured according to the method described above. • The cold work tool steel of item 5 of the patent application scope has 0100 / 〇SdA 60 j 400 $ 150%, of which "dA6〇χ "4〇〇" is the content of clathrates measured according to the method described in jismo555. M 1 is a cold work tool steel as described in item 6 of the patent application scope, which has a 0.10 / o ^ dA copy, ^ L50% 'where "dA60 x 400" is the content of the inclusion compound measured according to the method described in JISG0555. 60 X towel * Patent 围 around the 7th cold-working tool steel, which has the meaning of% ^ 必X 4〇0 J ^ «JIS 00555 method for inclusion content. X _" is the cold work tool steel as described in nsGG555, which makes the item 1 of the scope of the patent, and can be used at greater than or equal to 21 200536945 Quenched at 950C and less than or equal to 108 (TC) and obtained at 3.0 $ Gq $ 8.0. Gq is the particle size of the old Vosted iron after quenching, which is based on G0551 The measurement is carried out by the method described above. 18 · If the cold-working tool steel of item 2 of the patent application scope can be quenched at a temperature greater than 950 ° C and lower than or equal to 1080, and 30 gGq $ 80 Obtained, where Gq is the grain size of the old Vosted iron after quenching, which is measured according to the method described in G0551. 19. · The cold-working tool steel of item 3 of the patent application can be used at a temperature greater than Quenched at 950 ° C and less than or equal to 108 ° C, and 3x) gGq $ 800. 獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺寸，其係根巧 G0551中所述之方法進行測量。 2〇·如申請專利範圍第5項之冷作工具鋼，可藉由在大於 於950°C及小於或等於l〇8(TC之溫度下淬火，且3.0gGq$8 〇來 獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺寸，其係根§ G0551中所述之方法進行測量。 21·如申请專利範圍帛1〇 j員之冷作工具鋼，可藉由在大於 等於9贼及小於或等於l〇8(TC之溫度下淬火，且3 〇$叫^〇 來獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺 JISG0551中所述之方法進行測量。 八你很像 22·如申凊專利範圍帛11 j員之冷作工具鋼，可藉由 等於95(TC及小於或等於1080t：之溫度下泮火，且3 、= 來獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺 JIS G0551中所述之方法進行測量。 八你很爆 23·如申請專利範圍帛6項之冷作工具鋼，可藉由在大於 於950°C及小於或等於108(TC之溫度下淬火，且3.〇$Gqg8 〇來 獲得，其中Gq為淬火後的舊沃斯田鐵之顆粒尺寸， G0551中所述之方法進行測量。 宁很像b ，可藉由在大於或 ，且 3.0$Gq$8.0 24·如申請專利範圍第12項之冷作工具鋼 等於950°C及小於或等於1080°C之溫度下淬火 22 200536945 π纏η情述q之縣尺寸，其係根據 等於範圍第13項之冷作工具鋼，可藉由在大於或 f於95〇c及小於或等於1〇8叱之 卿別中所述q之斯田鐵之顆粒尺寸，其係根據 於範圍第7項之冷作工具鋼，可藉由在大於或等 於950C及小於或等於10贼之溫度 G〇55l中所述之方法進行測量/狀顆粒尺寸，其係根據瓜 更包含一或更多 27.如申請專利範圍第22項之 且 選擇自下列條件之元素： 0.01 wt%^Cu^2.0 Wt% ； 0.01 wt%^Ni^2.0 wt% ； (UOwto/ogCo^Uwt% ;以及 0.0003 wt%$B$〇e〇l〇 wt%。 28·如申請專利範圍帛14項之冷作 等於_及小於或#於1G8(rc之溫:n由在大^或Obtained, where Gq is the particle size of the old Vosted iron after quenching, which was measured according to the method described in G0551. 2．If the cold tool steel of item 5 of the scope of patent application is applied, it can be obtained by quenching at a temperature greater than 950 ° C and less than or equal to 108 ° C and 3.0gGq $ 80, where Gq is The grain size of the old Vosted iron after quenching is measured in accordance with the method described in § G0551. 21 · If a cold-working tool steel is applied for a patent scope of 帛 10j, it can be used at 9 or more. And quenched at a temperature of less than or equal to 108 (TC), and 30 yuan is called ^ 〇, where Gq is measured by the method described in the old Vosted iron particle rule JISG0551 after quenching. Like 22 · Russian patent scope 帛 11 j member of cold work tool steel, can be obtained by fire equal to 95 (TC and less than or equal to 1080t :, and 3, =, where Gq is the quenched Measured in the method described in JIS G0551 of the old Vostian iron. Yayou is very explosive23. If you apply for a cold-working tool steel with a scope of 6 patents, you can use it at a temperature greater than 950 ° C and less than or equal to Quenched at 108 ° C and obtained at 3.0 GQg80, where Gq is the granules of the old Vostian iron after quenching Inch, measured by the method described in G0551. Ning is very similar to b, but can be used at a temperature greater than or equal to 3.0 $ Gq $ 8.0 24. For example, the cold-working tool steel equal to 950 ° C and less than or equal to Quenched at a temperature of 1080 ° C 22 200536945 π Wound η Story q The size of the county is based on the cold work tool steel equal to the 13th item in the range. The particle size of the iron alloy of Q-steel as described in the 8th chapter is based on the cold-working tool steel according to the seventh item in the range. It can be used at a temperature of greater than or equal to 950C and less than or equal to 10 thieves. G〇55l The method described in the measurement / like particle size is based on melon which contains one or more 27. Such as the element of the scope of application for patent 22 and selected from the following conditions: 0.01 wt% ^ Cu ^ 2.0 Wt%; 0.01 wt% ^ Ni ^ 2.0 wt%; (UOwto / ogCo ^ Uwt%; and 0.0003 wt% $ B $ 〇e〇l〇wt%. 28. If the scope of the application for patent 14 cold work is equal to and less than or # 于 1G8 (The temperature of rc: n by Zai ^ or 來獲得，其中Gq為淬火後的舊沃斯田鐵之 JIS G0551中所述之方法進行測量。 、;、、八糸根據 29·如申請專利範圍第15項之冷你丁曰λ .. 等於95(TC及小於或等於灌叱之^度下由在=或〇 來獲得，其巾Gq為淬火後的舊沃斯mGq=8·0 ns G〇551中所述之方法進行測^相鐵之顆粒尺寸，其係根據 30·如申請專利範圍第28項之冷作 選擇自下列條件之元素： /、、’，更匕3 —或更多 0.010 wt%^Nb^0.10 wt% ； 0.005 wt%$Tag0.10 wt% ; 0.005 wt%^Ti^〇.l〇 wt% ； 23 200536945 0.005 wt%^Zr^0.10 wt% ； 0.005 wt%$Mg$0.10 wt% ;以及 0.005 wt%$REM$0.10 wt% 〇 十一、圖式：Obtained, where Gq is the method described in JIS G0551 of the old Vosted iron after quenching. According to 29, such as the 15th in the scope of the patent application, you can say that λ is equal to 95 (TC and less than or equal to the degree of irrigation, which is obtained by = or 0, and the towel Gq is After quenching, the old Voss mGq = 8 · 0 ns G0551 was used to measure the particle size of the phase iron, which is an element selected from the following conditions according to the cold work of 30 · such as the 28th in the scope of the patent application : / ,, ', more dagger 3 — or more 0.010 wt% ^ Nb ^ 0.10 wt%; 0.005 wt% $ Tag0.10 wt%; 0.005 wt% ^ Ti ^ 〇.10 wt%; 23 200536945 0.005 wt % ^ Zr ^ 0.10 wt%; 0.005 wt% $ Mg $ 0.10 wt%; and 0.005 wt% $ REM $ 0.10 wt% 〇11. Scheme: 24twenty four