200946696 六、發明說明： 【發明所屬之技術領域】 本發明係關於-種能較佳地適用於作為汽車用變速器之機 械零件的離合器片或同步環、離合器圓盤等中、且強度、沖孔 .加工性以及耐熱變形性均優異的冷軋鋼板及其製造方法。 【先前技術】 >飞車用變速ϋ#、由離合器片或同步環、離合器圓盤等構成， ©且發揮傳遞驅動力、及吸收因摩擦產生之熱的作用。上述零件 係藉由將鋼板沖孔成環狀而製造。變速器係藉由若干塊上述環 - 狀板材重疊而成為傳遞扭矩的構造，作為其功能，要求财磨耗 性及板材平坦度。因此，關於作為材料之鋼板的必要特性，要 求硬度、沖孔加工時之性狀（平坦度以及毛邊等之沖孔面性 狀）、以及加熱時之變形程度、即耐熱變形性均優良等。 先前以來，作為自動變速器（以下稱作AT)之離合器片用材 © 料，主要使用以JIS G3311為標準之機械構造用鋼中的S35c 冷軋鋼板。該S35C冷軋鋼板係由「鋼坯—熱軋->酸洗退火 —冷軋」之步驟而製造。S35C冷軋鋼板因含有大量c(〇. 35質 量％左右），故而熱軋鋼板之硬度較高，因此，為了碳化物之球 狀化及軟質化，必須於冷軋前實施幾小時以上之長時間的退 火。故而，就要求低價格之汽車零件而言，成本上非常不利。 專利文獻1中，揭示有一種冷軋前不對熱軋鋼板進行退火之 技術。亦即，提出一種藉由對C含量為〇. 25質量％以下之具有 098106119 3 200946696 軟質性的熱軋鋼板以50%以上之軋縮率進行冷軋，從而獲得能 確保所需之硬度及表面粗度且耐磨耗性及沖孔加工性優良之 AT離合器片用冷軋鋼板。然而，此種鋼板存在以下問題：因 冷軋時之殘留應力而導致沖孔加工時沖孔端面的性狀明顯惡 化，而且，當溫度上升時會產生熱應變，使得環狀產品之平坦 度明顯下降。 專利文獻2巾’作為改善上述冷軋後之殘留應力之技術，提 出-種AT離合||>j用冷軋鋼板’其對冷軋後之鋼板進錢用 ◎ 輥徑為300刪以上之大輥以1%左右之軋縮率於輕壓下進行軋 製’藉此，降低了殘留應力。然而，該方法中，導入至鋼板表 背面的應變之差減少’故而，壓製沖孔加工時的沖孔端面的性 狀會改善’但鋼板内部之殘留應力並不會消除，故而，溫度上 升時無法避免隨熱應變而產生變形，環狀產品之平坦度仍然會 明顯下降。 專利文獻3中，提出-種_酸洗等之鋼板表面粗度調整處❹ 理而達到最佳表面減、且與雜材之接著性❹的at離合 器片用鋼板。該鋼板經熱軋、酸洗後，較佳為以議〜綱。c 進仃3小相上退火以使碳化物成為雜化，隨後，以以以 上之軋縮轉㈣觀冷軋，錢進行峨表面減調整 處理’但與專利文獻i以及專利文獻2同樣，因冷札後之殘留 應力所導狀環狀產品之平坦度_顯下降未制解決。 」 專利文獻1 :日本專利特開2003-277883號公報 098106119 4 200946696 專利文獻2 :曰本專利特開2005-200712號公報 專利文獻3:日本專利特開2004-107722號公報 【發明内容】 ' 树明財效解決上述_者，其目的在於提供—種能較佳 >地適用於離合器片、離合器環、離合器圓盤等中、具有較高硬 度、且沖孔加工時的端面性狀以及溫度上升時的平坦度優異的 冷軋鋼板及其之有利的製造方法。 ® 以下，對本發明之詳細内容進行說明。 . 4了消除因先前之離合器片用鋼板所具有之殘留應變引起 .的弊端’只要並不如先前般直接將冷軋後之鋼板作為材料，而 是於冷乳後進行退火㈣已㈣殘留應變之冷延退火板作為 材料即可。然而’當藉由退火已完全再結晶時，無法獲得必要 的硬度。 因此’為解決該問題’發明者等人進行銳意討論後發現，並 ❹不藉由冷軋後之退火而使鋼組織成為完全再結晶_，而是成 為殘留有一部分未再結晶組織之部分再結晶組織，藉此，不僅 能確保所需之硬度’而且能減輕殘留應變引起之問題、亦即因 沖孔加工時之端面性狀的劣化、以及溫度上升時因熱應變引起 之平坦度的劣化。 亦即，發現：當再結晶組織與未再結晶組織共存時，再結晶 組織中未殘留軋製應變，故而，會相應地減少沖孔加工時端面 性狀的劣化或溫度上升時平坦度的劣化，且因未再結晶組織中 098106119 5 200946696 殘留有軋製應變，故而，藉由該一部分殘留應變及再結晶粒之 微細化，能確保必要的硬度。 進而’亦發現：對於鋼板之硬度而言’鋼成分中、尤其是c、 Μη以及P之作用較大，藉由含有適量之上述元素，能穩定地 獲得必要的強度。 本發明係依據上述觀點反覆研究而製成。 本發明之主要構成係如下所述。 1. 一種冷軋鋼板，其特徵在於：以質量％計，含有 C : 0· 01 〜〇· 15%、200946696 VI. TECHNOLOGICAL FIELD OF THE INVENTION [Technical Field] The present invention relates to a clutch disc or a synchronizing ring, a clutch disc or the like which is preferably used as a mechanical component of a transmission for an automobile, and has strength and punching. A cold-rolled steel sheet excellent in workability and heat deformation resistance and a method for producing the same. [Prior Art] > The speed change ϋ# for a flying vehicle is composed of a clutch plate, a synchronizing ring, a clutch disc, and the like, and functions to transmit a driving force and absorb heat generated by friction. The above parts are manufactured by punching a steel plate into a ring shape. The transmission is a structure that transmits torque by overlapping a plurality of the above-mentioned ring-shaped plates, and as its function, the wear resistance and the flatness of the sheet are required. Therefore, the properties required for the steel sheet as the material are required to be excellent in hardness, punching processing properties (flatness and punching surface properties such as burrs), and deformation at the time of heating, that is, heat deformation resistance. In the past, the S35c cold-rolled steel sheet in the steel for machine structural use based on JIS G3311 is mainly used as the material for the clutch disc of the automatic transmission (hereinafter referred to as AT). The S35C cold-rolled steel sheet is produced by the steps of "slab-hot rolling-> pickling annealing-cold rolling". Since the S35C cold-rolled steel sheet contains a large amount of c (about 35 mass%), the hardness of the hot-rolled steel sheet is high. Therefore, in order to spheroidize and soften the carbide, it is necessary to carry out a few hours or more before cold rolling. Annealing of time. Therefore, in terms of requiring low-priced automotive parts, the cost is very unfavorable. Patent Document 1 discloses a technique of not annealing a hot rolled steel sheet before cold rolling. That is, it is proposed to cold-roll a hot-rolled steel sheet having a softness of 098106119 3 200946696 having a C content of 0.25.5% by mass or less at a rolling reduction ratio of 50% or more, thereby obtaining a desired hardness and surface. A cold-rolled steel sheet for an AT clutch sheet excellent in thickness, wear resistance, and punching workability. However, such a steel sheet has the following problems: the characteristics of the punched end face are remarkably deteriorated during the punching process due to the residual stress at the time of cold rolling, and the thermal strain is generated when the temperature rises, so that the flatness of the annular product is remarkably lowered. . In the technique of improving the residual stress after the cold rolling, the patent document 2 towel proposes a type of cold-rolled steel sheet for AT-coupling||>j, which is used for the steel sheet after cold-rolling, and has a roll diameter of 300 or more. The large roll is rolled at a rolling reduction of about 1% under light pressure, thereby reducing residual stress. However, in this method, the difference in strain introduced into the back surface of the steel sheet is reduced. Therefore, the properties of the punched end surface during press punching are improved, but the residual stress inside the steel sheet is not eliminated, so that the temperature cannot rise. Avoid deformation with thermal strain, and the flatness of the ring product will still drop significantly. In Patent Document 3, a steel sheet for an at-wafer sheet in which the surface roughness adjustment of the steel sheet such as pickling is performed to achieve optimum surface reduction and adhesion to the miscellaneous material is proposed. After the steel sheet is hot rolled and pickled, it is preferably in the form of a steel sheet. c. The small phase of the enthalpy 3 is annealed to make the carbides hybrid. Then, the crucible surface reduction treatment is performed by the above-mentioned rolling reduction (four) cold rolling, but the same as in Patent Document i and Patent Document 2, The flatness of the ring-shaped product guided by the residual stress after the cold is not resolved. Patent Document 1: Japanese Patent Laid-Open Publication No. 2003-277883 No. 098106119 4 200946696 Patent Document 2: Japanese Patent Laid-Open Publication No. Hei No. 2005-200712 Patent Publication No. JP-A-2004-107722 In order to solve the above problems, the purpose of the invention is to provide a high-hardness, high-hardness, and end face properties and temperature rise during punching processing, such as a clutch plate, a clutch ring, a clutch disc, and the like. A cold rolled steel sheet excellent in flatness at the time and an advantageous manufacturing method thereof. ® The following details the details of the present invention. 4. The disadvantage of eliminating the residual strain caused by the steel plate for the previous clutch plate is as long as the steel plate after cold rolling is not directly used as the material, but is annealed after cold milk (4) (4) residual strain The cold-annealed sheet can be used as a material. However, when it is completely recrystallized by annealing, the necessary hardness cannot be obtained. Therefore, in order to solve this problem, the inventors and others have made a keen discussion and found that the steel structure is not completely recrystallized by annealing after cold rolling, but becomes a part of the unrecrystallized structure remaining. By crystallizing the structure, not only the required hardness can be ensured, but also the problem caused by the residual strain, that is, the deterioration of the end face property at the time of punching processing and the deterioration of the flatness due to the thermal strain at the time of temperature rise can be alleviated. In other words, it has been found that when the recrystallized structure and the non-recrystallized structure coexist, the rolling strain does not remain in the recrystallized structure, so that the deterioration of the end face property during the punching process or the deterioration of the flatness at the time of temperature rise is correspondingly reduced. Further, since the rolling strain remains in the unrecrystallized structure of 098106119 5 200946696, the necessary hardness can be ensured by the partial residual strain and the refinement of the recrystallized grains. Further, it has been found that the steel component has a large effect on the hardness of the steel sheet, in particular, c, Μ, and P, and the necessary strength can be stably obtained by containing an appropriate amount of the above elements. The present invention has been made in the light of the above findings. The main constitution of the present invention is as follows. A cold-rolled steel sheet characterized by containing C: 0·01 〇 〇 15% by mass%
Si : 0. 03%以下、 Μη : 0. 1〇〜〇. 70%、 Ρ : 0. 025%以下、 S : 0. 025%以下、 Α1 : 0.01 〜0.05%以及 Ν : 0. 008%以下，且 該等成分滿足下式（1)之關係， (C%) + 〇. 15x(Mn°/〇) + 0. 85x(P%)^0.21 ....··(ι) 其中，（Μ%)表示元素Μ之含量（質量％) 其餘部分係由Fe以及不可避免的雜質組成、且係由肥粒鐵 平均粒佐為2〜1〇 “in、未再結晶率為25%以上、9〇%以下之部 分再結晶組織構成，以洛氏硬度HRB計，硬度為83以上。 2. —種冷軋鋼板之製造方法，其特徵在於：將以質量％計、 098106119 6 200946696 含有 C : 0.01 〜0.15%、Si: 0. 03% or less, Μη: 0. 1〇~〇. 70%, Ρ: 0. 025% or less, S: 0. 025% or less, Α1: 0.01 to 0.05%, and Ν: 0. 008% or less And the components satisfy the relationship of the following formula (1), (C%) + 〇. 15x(Mn°/〇) + 0. 85x(P%)^0.21 ....··(ι) where, ( Μ%) indicates the content of the element ( (% by mass) The rest is composed of Fe and unavoidable impurities, and is based on the average grain size of the granules of the granules of 2 to 1 〇 "in, the rate of non-recrystallization is 25% or more, a part of the recrystallized structure of 9 % or less, and a hardness of 83 or more in terms of Rockwell hardness HRB. 2. A method for producing a cold-rolled steel sheet, characterized in that C: 098106119 6 200946696 is contained in mass %: 0.01 to 0.15%,
Si : 0.03%以下、 ' Μη : 0.10〜0. 70%、 ' P :0.025%以下、 S : 0. 025%以下、 Α1 : 0. 01 〜0. 05%以及 φ Ν : 0. 008%以下，且 該等成分滿足下式（1)之關係’ (C%) + 0.15χ(Μη%) + 0. 85χ(Ρ%)^21 ……（1) 其中，（Μ%)表示元素Μ之含量（質量％) 且其餘部分由Fe以及不可避免的雜質組成之鋼坯，以 變態點以上之加工溫度進行熱軋，且以580〜75(TC之捲取溫 度進行捲取，隨後進行酸洗，之後以65%以上之軋縮率進行a ❿軋，此後，藉由連續退火而以680X：以下之溫度進行退火。 【實施方式】 以下’對本發明進行具體說明。 首先，對於本發明中對鋼板之組織進行上述限定的理由進行 說明。 肥粒鐵平均粒徑：2〜 為了確保充分硬度，肥粒鐵平均粒徑必須處於適當之範圏 内，若肥_平均粒徑超過1G叫彳無法獲騎冑之硬度。 098106119 200946696 孔性=右小於2 則硬度會過度上升，而導致壓製沖 。肥粒鐵平均粒徑較佳為4〜8 _之範圍。 再者|發明中’作為肥粒鐵平均粒徑，係藉由對鋼板之札 士方向上的板厚剖面進行觀察，依據爪G _(隨附說明） 中揭不之切割法而求出。 未再結晶率：25%以上、90%以下 本發明之純鋼㈣最大魏係，絲再結晶域與再結晶 、.織構成之部分再結m為確保鋼板之硬度，必須含有殘 =由冷軋時解鋼板之軋製應變之—定量的未再結晶粒。為提 高沖孔加工性以及耐熱變形性，亦必須含有—定量之再結晶組 織亦即’為同時具有較尚的硬度及沖孔加工性、耐熱變形性， 重要的是未再結晶組織與再結晶組織的比例。 此處，因根據軋製應變之效果而獲得所需之硬度，故未再結 a曰率必須達到25%以上。然而，若未再結晶率超過9〇%，則再 、、、。曰a粒會明顯減少，沖孔加工性會劣化，且殘留應變變得過大 且平坦度亦劣化，故而，將未再結晶率設為9〇%以下。更佳為， 40%以上、80%以下之範圍。 再者’未再結晶率係藉由觀察鋼板之軋製方向上的板厚剖 面，求出整個組織中未再結晶組織所占之比例（面積比），從而 將其視為未再結晶率。 繼而，對於本發明中對鋼板之成分組成進行上述限定的理由 進行說明。再者，成分中之「％」符號，只要無特別說明，均 098106119 8 200946696 表示質量％。 C:0. 01 〜0. 15% C係對冷軋鋼板之硬度以及耐磨耗性而言較重要之元素，若 ' C量較高則硬度以及耐磨耗性均會上升。故而，為獲得所需之 • 硬度以及耐磨耗性，須使c量達到0.01%以上。另一方面，若 C量超過0. 15%則沖孔加工性會劣化。而且，沖孔時之表背面 的變形應變之差會變大，進而’升溫時因熱應變而引起之變形 ❹會變大，故而，沖孔材之平坦度會劣化。故而，將c量限定於 0. 01〜0.15%之範圍。C量較佳為〇. 〇5〜〇. 15%之範圍，更佳為 0. 10〜0. 15%之範圍。Si : 0.03% or less, ' Μ η : 0.10 to 0. 70%, ' P : 0.025% or less, S : 0. 025% or less, Α 1 : 0. 01 to 0. 05% and φ Ν : 0. 008% or less And the components satisfy the relationship of the following formula (1) '(C%) + 0.15χ(Μη%) + 0. 85χ(Ρ%)^21 (1) where (Μ%) represents the element A billet having a content (% by mass) and the remainder consisting of Fe and unavoidable impurities is hot-rolled at a processing temperature above the metamorphic point, and coiled at a coiling temperature of 580 to 75 (TC), followed by pickling. Thereafter, a rolling is performed at a rolling reduction ratio of 65% or more, and thereafter annealing is performed at a temperature of 680X: or less by continuous annealing. [Embodiment] Hereinafter, the present invention will be specifically described. First, for the steel sheet of the present invention The reason for the above-mentioned limitation of the structure is described. The average particle size of the fertilized iron: 2~ In order to ensure sufficient hardness, the average particle size of the fertilized iron must be within an appropriate range, and if the average particle size exceeds 1G, it cannot be obtained. The hardness of 胄. 098106119 200946696 Porosity = right less than 2, the hardness will rise excessively, resulting in pressurization The average grain size of the ferrite iron is preferably in the range of 4 to 8 _. In addition, in the invention, the average particle diameter of the ferrite is observed by the thickness profile of the steel plate in the direction of the slab, according to the claw G. _ (following instructions) is obtained by the cutting method. The rate of non-recrystallization is 25% or more and 90% or less. The pure steel of the present invention (4) is the largest Wei system, the silk recrystallized domain and the recrystallization, and the weave. In order to ensure the hardness of the steel sheet, the partial re-make m must contain the residual non-recrystallized grains from the rolling strain of the steel sheet during cold rolling. In order to improve the punching workability and heat deformation resistance, it is necessary to contain - quantitative The recrystallized structure also means that it has a relatively high hardness and punching workability and heat deformation resistance, and the ratio of the unrecrystallized structure to the recrystallized structure is important. Here, the effect is obtained according to the effect of the rolling strain. The required hardness is not more than 25%. However, if the recrystallization rate is more than 9〇%, the 曰a particles will be significantly reduced, and the punching processability will be deteriorated. The residual strain becomes too large and the flatness is also deteriorated, so it will not be The crystallization ratio is set to be 9% by mass or less, more preferably 40% or more and 80% or less. Further, the 'no recrystallization ratio is obtained by observing the thickness profile of the steel sheet in the rolling direction. The proportion (area ratio) of the non-recrystallized structure is regarded as the non-recrystallization rate. Next, the reason for limiting the chemical composition of the steel sheet in the present invention will be described. The symbol is 098106119 8 200946696 for mass% unless otherwise specified. C:0. 01 ～0. 15% C is an important element for the hardness and wear resistance of cold-rolled steel sheets. Higher hardness and wear resistance will increase. Therefore, in order to obtain the required hardness and wear resistance, the amount of c must be 0.01% or more. On the other hand, if the amount of C exceeds 0.15%, the punching workability is deteriorated. Further, the difference in deformation strain between the front and back surfaces at the time of punching becomes large, and the deformation due to thermal strain at the time of temperature rise becomes large, so that the flatness of the punched material is deteriorated. Therefore, the amount of c is limited to a range of 0.01 to 0.15%. The amount of C is preferably 〇. 〇5~〇. 15% of the range, more preferably 0. 10~0.
Si : 0. 03%以下 若Si量超過0.03%，則熱軋鋼板之表面上容易因鏽而產生 缺陷，而且，即便於熱軋之後進行酸洗，亦難以完全除去鏽。 故而，熱軋鋼板表面上容易因鏽而產生缺陷，而使鋼板之表面 ©狀態惡化，結果’亦會對冷軋後完成退火之鋼板的表面性狀產 生不佳影響。故而，將Si量限定為〇· 〇3%以下。較佳為〇. 〇2% 以下’亦可為G%。再者’當前之提煉技術下，隨著製鋼成本 的顯著上升，Si量之下限為〇.〇〇5%左右。 Μη : 0. 1〇〜〇· 7〇〇/0 Μη係具有將鋼中作為雜質而存在之S作為析出物(MnS)而使 其固定’從而減少S之不佳影響之作用的元素。為獲得此效 果’必須使Μη量在〇. 10%以上。另一方面，若Mn量超過〇, 7〇%, 098106119 9 200946696 則會導致鋼板的硬度過度上升從而導致沖孔加工性下降。其原 因在於，藉由Μη的固溶強化而使鋼強化。而且’若Mn量超過 0. 7(U，則熱軋鋼板之表面容易因鏽而產生缺陷，而且，即便 於熱軋之後進行酸洗，亦難以完全除去鏽。結果，亦會對冷軋 後完成退火之鋼板的表面性狀造成不良影響，無法獲得所需之 表面粗度。故而，將Μη量限定於〇. 1〇〜〇. 70%之範圍。再者， Μη罝較佳為〇. 50%以下，更佳為Μη量在〇. 20〜0· 50%之範圍。 Ρ : 0. 025%以下 Ρ係藉由固溶強化而使鋼強化的元素。然而，若ρ量超過 0‘ 025%，則會導致鋼坯破裂或鋼板表面產生缺陷❶而且，會導 致鋼的硬度明顯上升，從而導致沖孔加工性劣化。故而，將ρ 罝限定為0. 025%以下。Ρ量較佳為〇 023%以下。再者，當ρ 量未滿0.01%時，其對鋼強化之效果較小，故而較佳為〇 〇ι% 以上。 S : 0. 025%以下 s係鋼中作為雜質而存在之元素。尤其是當含有之s超過 0. 025%時，會形成粗大的介在物，以此為起點而成為加工破裂 之原因’從而導致沖孔加工性明顯下降。而且，s對熱乳鋼板 之鏽剝離性亦有影響，若s量超過〇. 〇25%，則酸洗後之表面 性狀會劣化，結果，冷軋後完成退火之鋼板的表面粗度亦會更 大。故而，將S量限定為〇. 025%以下。較佳為〇. 〇2〇%以下。 A1 : 0. 01 〜〇. 〇5% 098106119 10 200946696 ==柿賴0有之元素。未料⑽時， 無法獲付絲之賴效果。另_方面，即便A丨量 脫酸效果會翻姊。故而，將A丨纽定為㈣〜0鹰之 範圍。較佳為，A1量在0. 03〜0. 05%之範圍。 N : 0.008%以下 1係鋼巾作為雜質转在之元素，若N量超過M咖，則鋼 ❹ ❹ 板會過度魏㈣致沖孔加讀下降。故而，將n量限定為 0. 008%以下。較佳為〇. 〇〇5%以下。 疋 以上，係對必須成分進行說明，但本發日种之各成分僅滿足 上述組成範圍並不夠，尤其是C、Mn、P必須滿足下式⑴。 c* = (C%) + 0.15χ(Μη%) + 0. 85χ(Ρ%)^2ι··.···⑴ 本發明中，對鋼板硬度影響較大之元素係c、Mn以及p，該 c氺係本發明之鋼板的硬度指標。關於c氺之限定理由，使用 根據後述之實施例1製成的圖1進行說明與硬度（HRB) 之間具有圖1所示之比例關係，當c*之值為Q21以上時， 硬度達到所需之83 HRB以上。故而，本發明中，使c*滿足 上式（1)之條件。 本發明之鋼板中，上述以外的成分為Fe以及不可避免的雜 質。但是’只要在不影響本發明之效果的範圍内，則可含有上 述以外之成分。 繼而’對於本發明中對鋼板之硬度以及表面粗度進行上述限 定的理由進行說明。 098106119 11 200946696 硬度（HRB) : 83以上 、變速器係藉由將鋼板沖孔成環狀所得之若干塊板材重疊而 成為傳遞扭矩之構造。故而，作為使用之鋼板，對耐磨耗性有 要求，必須具有能確㈣磨耗性之硬度⑽B) : 83以上。當硬 度未滿83 _時，會導致财絲性下降，故而，必須達到83 _以上。料，若硬度超過95 HRB，則會導致沖孔形狀產生 問題或冲孔時鋼板產生破裂、龜裂，故而較佳為95 HRB以 下。 而且’為提高耐絲性，較佳絲錄度較小，且本發明之 〇 鋼板中，將表面粗度以算術平均粗度：Ra計，較佳為〇 3 _ 以下。再者’作為在不會使製造成本明顯上升之範圍内能達到 的表面粗度之下限值，以當前的技術水平，為〇ι㈣左右。 繼而，對於本發明之冷軋鋼板之製造方法進行說明。 將具有上述成分組成之鋼坯，以An變態點以上之加工溫度 y…、軋且以580〜750 C之捲取溫度進行捲取，進而對該 ◎ 熱軋鋼板進行酸洗，隨後以65%以上之軋縮率進行冷軋，之後， 於連續退火爐中以68(rc#下之溫度進行退火。 鋼趣之製造方法中，並無特別限制，只要按常法實施即可。 關於鋼坯之熔化以及鑄造，自生產效率以及鋼坯品質之觀點考 慮，較佳為使用轉爐以及連續铸造機來進行。 關於熱軋，自熱軋鋼板之品質及熱軋之效率等方面考慮，加 工溫度必須為An變態點以上。當加工溫度未滿An變態點時， 098106119 12 200946696 會促進熱軋鋼板上肥粒鐵之變態，從而產生表層上形成粗大顆 粒而導致硬度下降的問題。此後之捲取中，捲取溫度必須在 580〜750°C之範圍内。當捲取溫度低於58(rc時，結晶粒會過 度微細化’而且’會因冷卻應變而使熱軋鋼板硬質化從而阻礙 冷軋性。另一方面，當捲取溫度超過75〇〇c時，捲取後肥粒鐵 平均粒徑會粗大化，而且，會過度促進鋼板表面之鏽的生成， 從而使表面性狀劣化，且使表面粗度明顯劣化。捲取溫度較佳 〇 為600〜720°C之範圍。再者，Ar3變態點可藉由使用示差熱膨 脹計等之熱膨脹測定而求出。 按常法對熱軋鋼板進行酸洗而除去鋼板表面上的鏽之後，對 其進行冷軋。冷軋之軋縮率必須為65%以上。於冷軋後實施之 退火中，為使肥粒鐵粒微細化而提高硬度、且為降低表面粗 度，必須具有上述軋縮率。另一方面，軋縮率之上限並無特別 限定，但當以超過85%之高軋縮率進行冷軋時，擔心會導致軋 ❿製後鋼板之形狀不佳或板厚精度下降、因冷軋機之軋製負荷過 大而導致生產性下降等。故而，軋縮率較佳為85%以下。 冷軋後之鋼板係藉由連續退火爐而實施退火。本發明中，尤 其重要的是於冷軋後以再結晶結束溫度以下之溫度進行退 火。當退火溫度超過再結晶結束溫度時，退火後幾乎100%的 組織都成為再結晶組織，故而，冷軋時導入之軋製應變會消 除。故而，無法獲得所需之較高的硬度。因此，藉由使退火溫 度為再結晶結束溫度以下，可形成混合有未再結晶粒與再結晶 098106119 13 200946696 ♦ 粒之部分再結晶組織。 方去中，未再結晶率之比率係由退火溫度決定藉 由使=火=度處於68代以下，可使未再結晶率達到娜以 、度之下限並無特別限定，但自連續爐之溫度、以及 ¥兄之控制性及生產性方面考慮較佳為咖。〇以上。而且， 退火後之冷部迷度並無特別限定，較佳為左右。進 而，該冷卻過程中，所謂於320〜420X：之溫度範圍内進行保 μ處理係、對於鋼板之形狀穩定性、或實施調質軋壓時調質軋❹ 壓中的表面粗度之調整方面較有利。 再者’未再結晶率可根據退火溫度而適當調整。作為未再結 曰曰曰率與退火溫度之關係，可例如預先以如下方式求出外觀上之 未再結晶率與獲得該未再結晶率之退火溫度間的關係，再根據 5亥關係調整為獲得所需之未再結晶率的退火溫度即可。 (外觀上之未再結晶率— HRB(S))xl00(%) ❹ 其中， • HRB(P):係以規定溫度進行退火後之鋼板的洛氏硬度（B 標尺） • HRB(S):係以完全成為再結晶組織之溫度進行退火後之鋼 板的洛氏硬度（B標尺） • HRB(H):係以完全不會再結晶之溫度進行退火後之鋼板的 洛氏硬度（B標尺） 098106119 14 200946696 · 、再者，計算上述外觀上之未再結晶率時，為除去退火後根據 冷卻條件而產生之硬度的變動，較佳為求出對冷乳後之鋼板進 行退火後再經水淬火之鋼板的硬度。 • 又’亦可預先求出如上所述求出之外觀上之未再結晶率與鋼 板硬度間的關係’再根據該關係，依據退火後鋼板之硬度求出 外觀上之未再結晶率，來推斷鋼板之未再結晶率。 亦了對退火後之冷軋鋼板利用調質軋遷於輕壓下進行軋 ❹製。此目的在於調整表面粗度且進一步改善硬度。例如，當設 成較佳之表面粗度：Rag0. 3 時，較佳為，以伸長率計， 軋縮率為2%以上。再者，軋縮率之上限並無特別限定，但於 過高之軋縮率下’鋼板之形狀會產生偏差。又，考慮到進行調 質軋壓之軋製機的能力，較佳為，以伸長率計，軋縮率為5% 以下。 [實施例] ❹[實施例1] 將具有表1所示之成分組成的鋼坯加熱至12〇〇°c，之後， 以Ar3變態點以上之加工溫度進行熱軋，繼而，於鋼片輸送台 上冷卻後以60(TC進行捲取，使熱軋鋼板之板厚成為5腿。隨 • 後’利用酸洗除去鏽，之後以70%之軋縮率進行冷軋，製成板 厚為丨.5 mm之冷軋鋼板。將該冷軋鋼板脫脂之後，利用連續 退火爐以650°C實施退火。退火時間為1分鐘。退火之後，使 鋼板以10°C/s之速度冷卻，之後’以320〜42(TC保溫2. 5分 098106119 15 200946696 -’之後冷郃至室溫。進而’利用調質軋壓線以&〇 縮率（伸長率）於輕壓下進行軋製。 匕 以此獲得之鋼板的肥粒鐵平均粒徑、未再結晶率、表面 度、硬度、沖孔加工性以及耐熱變形性的調查結果如表1所面示粗 再者，各調查項目係以如下所述之方法測定。 不。 肥粒鐵平均粒徑 自鋼板切出試料（軋製方向上的板厚剖面）進行研磨後，呈 出肥粒鐵結晶粒界’彻好顯微鏡以_倍之倍率觀察，現 攝相片’之後，以利用JIS G _(隨附說明）中記載之、切^ 法之鋼的肥粒鐵粒度測試方法（JIS G 〇552(1998》為義 D 計算。 ^準進行 未再結晶率 關於未再結晶率’與計算肥粒鐵平均粒㈣相同，對礼製方 向上的板厚剖面以8GG倍之倍率進行觀察’求出未再結晶 之面積率，將此作為未再結晶率。 ㉝ 表面粗度 依據JIS B0601中規定之測定方法，求出算術平均粗度：^。 硬度（HRB) ° 自鋼板切出大小為2Gx6Gmm之試料，依據JISZ 2245中規 定之洛氏硬制試方法騎啦。測定細B標尺於ι〇點進 行，將其平均值作為硬度（HRB)。 沖孔加工性 098106119 200946696 藉由壓製式沖孔機’以沖孔尺寸：内徑14〇mmx外徑16〇咖、 間隙：板厚之10%(板厚：1.5 mm)沖孔後製成環狀測試片，之 後，對鋼板軋製剖面上之沖孔端面利用倍率為1〇〜2〇倍的光 學顯微鏡進行觀察，按如下標準進行評估。 *·良好（〇）：沖孔端面上無龜裂或孔隙、且未產生毛邊或極 端的壓陷。 •不佳（X)冲孔端面上產生龜裂或孔隋:、或者產生毛邊。 Φ 耐熱變形性 對與經過沖孔加工性評估者相同之環狀測試片，以綱1加 、、〜刀鐘之後’使其空冷，以該測試片到達室溫時的翹曲量 進仃3平估。趣曲量只要在01 mm以下，則可視為良好。 麵曲量之測定係以如下方式進行。經加熱空冷後之 測=材’利用#_以上之剛砂紙(emery卿er)對兩面進行 後，將測試材置於壓盤上，使用接觸式之高度規測定出 圓周方向上的10處的高度，且求出與測微計測定出之同—产 的板厚間之差’將其最大值作馳曲量。 % 098106119 17 200946696Si: 0.03% or less When the amount of Si exceeds 0.03%, defects are likely to occur on the surface of the hot-rolled steel sheet due to rust, and it is difficult to completely remove rust even after pickling after hot rolling. Therefore, the surface of the hot-rolled steel sheet is liable to be defective due to rust, and the surface of the steel sheet is deteriorated. As a result, the surface properties of the steel sheet which is annealed after cold rolling are adversely affected. Therefore, the amount of Si is limited to 〇·〇3% or less. Preferably, 〇. 〇 2% or less 'may also be G%. Furthermore, under the current refining technology, as the cost of steelmaking increases significantly, the lower limit of the amount of Si is about 〇〇.〇〇5%. Μη: 0. 1〇~〇·7〇〇/0 Μ η is an element which has an effect of reducing S as a precipitate (MnS) by using S as an impurity in steel to reduce the adverse effect of S. In order to obtain this effect, the amount of Μη must be 〇. 10% or more. On the other hand, if the amount of Mn exceeds 〇, 7〇%, 098106119 9 200946696, the hardness of the steel sheet is excessively increased, resulting in a decrease in punchability. The reason is that the steel is strengthened by solid solution strengthening of Μη. Further, if the amount of Mn exceeds 0.7 (U), the surface of the hot-rolled steel sheet is liable to be defective due to rust, and even if pickling is performed after hot rolling, it is difficult to completely remove rust. As a result, it is also possible after cold rolling. The surface properties of the annealed steel sheet are adversely affected, and the desired surface roughness cannot be obtained. Therefore, the amount of Μη is limited to the range of 〇.1〇~〇. 70%. Further, Μη罝 is preferably 〇. 50. More preferably, the amount of Μη is in the range of 〜. 20~0· 50%. Ρ : 0. 025% or less 元素 is an element which strengthens steel by solid solution strengthening. However, if the amount of ρ exceeds 0' 025 % , 则会 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢 钢023% or less. Further, when the amount of ρ is less than 0.01%, the effect on steel strengthening is small, so it is preferably 〇〇% or more. S: 0. 025% or less is present as an impurity in the steel. The element, especially when it contains more than 0.025%, it will form a coarse intervening material. However, it becomes the cause of the fracture of the process, which results in a significant decrease in punching workability. Moreover, s also affects the rust peelability of the hot-milk steel plate. If the amount of s exceeds 〇. 〇25%, the surface properties after pickling may deteriorate. As a result, the surface roughness of the steel sheet which is annealed after cold rolling is also greater. Therefore, the amount of S is limited to 0.25% or less, preferably 〇. 〇2〇% or less. A1 : 0. 01 〇 〇 5% 098106119 10 200946696 == Persimmon 赖 has some elements. Unexpected (10), can not be paid for the effect of silk. Another _ aspect, even A 丨 amount of deacidification effect will be turned over. Therefore, A 丨 button The range of (4) to 0 eagle. Preferably, the amount of A1 is in the range of 0. 03~0. 05%. N: 0.008% or less, the 1 series steel towel is transferred as an impurity element, if the amount of N exceeds M coffee, Then, the steel ❹ ❹ 会 会 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四 四However, it is not enough that the components of the present invention only satisfy the above composition range, especially C, Mn, and P must satisfy the following formula (1): c* = (C%) + 0.15 χ (Μη%) + 0. 85χ(Ρ%)^2ι······ (1) In the present invention, the elements C, Mn, and p which have a large influence on the hardness of the steel sheet are the hardness indexes of the steel sheet of the present invention. The reason for the limitation of the crucible is as shown in Fig. 1 which is made according to the first embodiment described later, and has a proportional relationship with the hardness (HRB) as shown in Fig. 1. When the value of c* is more than Q21, the hardness is required. 83 HRB or more. Therefore, in the present invention, c* is satisfied to satisfy the condition of the above formula (1). In the steel sheet of the present invention, the components other than the above are Fe and unavoidable impurities. However, the components other than the above may be contained as long as they do not impair the effects of the present invention. Next, the reason for limiting the hardness and surface roughness of the steel sheet in the present invention will be described. 098106119 11 200946696 Hardness (HRB): 83 or more. The transmission is a structure that transmits torque by superimposing a plurality of sheets obtained by punching a steel plate into a ring shape. Therefore, as the steel sheet to be used, there is a demand for wear resistance, and it is necessary to have a hardness (10) B) which is capable of (four) abrasion resistance: 83 or more. When the hardness is less than 83 _, it will lead to a decline in the financial property, so it must reach 83 _ or more. If the hardness exceeds 95 HRB, the shape of the punched hole may be caused or the steel sheet may be cracked or cracked at the time of punching, and therefore it is preferably 95 HRB or less. Further, in order to improve the yarn resistance, the wire thickness is preferably small, and in the steel sheet of the present invention, the surface roughness is represented by arithmetic mean roughness: Ra, preferably 〇 3 _ or less. Furthermore, as the lower limit of the surface roughness which can be achieved within a range in which the manufacturing cost is not significantly increased, the current technical level is about ( (4). Next, a method of producing the cold rolled steel sheet of the present invention will be described. The steel slab having the above composition is wound at a processing temperature y... above the An transformation point, rolled and wound at a coiling temperature of 580 to 750 C, and the ◎ hot rolled steel sheet is pickled, followed by 65% or more. The rolling reduction is performed by cold rolling, and then annealing is performed in a continuous annealing furnace at a temperature of 68 (rc#). The method for producing the steel is not particularly limited, and may be carried out by a usual method. And casting, from the viewpoint of production efficiency and slab quality, it is preferably carried out using a converter and a continuous casting machine. Regarding hot rolling, considering the quality of the hot-rolled steel sheet and the efficiency of hot rolling, the processing temperature must be an An Above the point. When the processing temperature is less than the An abnormal point, 098106119 12 200946696 will promote the metamorphosis of the ferrite and iron on the hot-rolled steel sheet, thereby causing the problem that the coarse particles are formed on the surface layer and the hardness is lowered. In the subsequent coiling, the coiling is performed. The temperature must be in the range of 580 to 750 ° C. When the coiling temperature is lower than 58 (rc, the crystal grains will be excessively refined 'and 'will harden the hot rolled steel sheet due to the cooling strain from On the other hand, when the coiling temperature exceeds 75 〇〇c, the average grain size of the ferrite iron after the coiling is coarsened, and the rust formation on the surface of the steel sheet is excessively promoted, thereby deteriorating the surface properties. Further, the surface roughness is remarkably deteriorated. The coiling temperature is preferably in the range of 600 to 720 ° C. Further, the Ar 3 transformation point can be determined by thermal expansion measurement using a differential thermal dilatometer or the like. The rolled steel sheet is pickled to remove rust on the surface of the steel sheet, and then cold rolled. The cold rolling has a rolling reduction ratio of 65% or more. In the annealing performed after cold rolling, in order to refine the ferrite particles In order to reduce the hardness and to reduce the surface roughness, it is necessary to have the above-described rolling reduction ratio. On the other hand, the upper limit of the rolling reduction ratio is not particularly limited, but when cold rolling is performed at a high reduction ratio of more than 85%, there is a fear that it may cause After rolling, the shape of the steel sheet is poor, the thickness accuracy is lowered, the rolling load of the cold rolling mill is too large, and the productivity is lowered. Therefore, the rolling reduction ratio is preferably 85% or less. Annealing by continuous annealing furnace. The invention It is especially important to anneal at a temperature below the recrystallization end temperature after cold rolling. When the annealing temperature exceeds the recrystallization end temperature, almost 100% of the microstructure becomes a recrystallized structure after annealing, so that it is introduced during cold rolling. The rolling strain is eliminated. Therefore, the required higher hardness cannot be obtained. Therefore, by making the annealing temperature below the recrystallization end temperature, a portion in which unrecrystallized grains and recrystallized 098106119 13 200946696 ♦ particles are formed can be formed. Recrystallization of the structure. The ratio of the unrecrystallized ratio is determined by the annealing temperature, and the lower limit of the degree of non-recrystallization is not limited, but the lower limit of the degree of non-recrystallization is not limited. It is preferred from the viewpoint of the temperature of the continuous furnace and the controllability and productivity of the brother. 〇 Above. Further, the degree of cold portion after annealing is not particularly limited, and is preferably left and right. Further, in the cooling process, the so-called micro-treatment in the temperature range of 320 to 420X: the shape stability of the steel sheet, or the adjustment of the surface roughness in the quenching and rolling rolling at the time of quenching and temper rolling is performed. More favorable. Further, the rate of no recrystallization can be appropriately adjusted depending on the annealing temperature. As a relationship between the unre-cracking ratio and the annealing temperature, for example, the relationship between the unrecrystallized ratio in appearance and the annealing temperature at which the non-recrystallization ratio is obtained can be obtained in advance as follows, and then adjusted to 5 The desired annealing temperature without the recrystallization rate can be obtained. (No recrystallization rate in appearance - HRB(S)) xl00(%) ❹ where: • HRB(P): Rockwell hardness (B scale) of steel sheet after annealing at a specified temperature • HRB(S): Rockwell hardness (B scale) of steel sheet after annealing at a temperature at which it is completely recrystallized. HRB (H): Rockwell hardness (B scale) of steel sheet after annealing at a temperature that does not recrystallize completely 098106119 14 200946696 · Furthermore, when calculating the non-recrystallization rate in the above appearance, in order to remove the change in hardness due to the cooling condition after annealing, it is preferable to obtain a steel sheet after annealing the cold milk and then pass through the water. The hardness of the hardened steel plate. • In addition, the relationship between the unrecrystallized ratio and the hardness of the steel sheet obtained as described above can be obtained in advance. Based on this relationship, the apparent recrystallization rate can be obtained from the hardness of the steel sheet after annealing. The rate of non-recrystallization of the steel sheet was inferred. The cold-rolled steel sheet after annealing is also subjected to rolling and rolling under gentle pressing. The purpose is to adjust the surface roughness and further improve the hardness. For example, when a preferred surface roughness: Rag 0.3, is used, it is preferred that the reduction ratio is 2% or more in terms of elongation. Further, the upper limit of the rolling reduction ratio is not particularly limited, but the shape of the steel sheet may vary depending on the excessively high rolling reduction ratio. Further, in consideration of the ability of the rolling mill for performing the temper rolling, it is preferable that the rolling reduction ratio is 5% or less in terms of elongation. [Examples] 实施 [Example 1] A slab having the composition shown in Table 1 was heated to 12 ° C, and then hot rolled at a processing temperature of not more than the Ar 3 transformation point, and then on a steel sheet conveying table. After cooling, it was wound up at 60 (TC, so that the thickness of the hot-rolled steel sheet became 5 legs. After the rust was removed by pickling, and then cold-rolled at a shrinkage rate of 70% to obtain a sheet thickness of 丨. .5 mm cold-rolled steel sheet. After degreasing the cold-rolled steel sheet, annealing was performed at 650 ° C in a continuous annealing furnace. The annealing time was 1 minute. After annealing, the steel sheet was cooled at a rate of 10 ° C / s, after ' After 320~42 (TC insulation 2. 5 minutes 098106119 15 200946696 - 'after cooling to room temperature. Then 'using the quenching and rolling line to & shrinkage rate (elongation) under gentle pressure rolling. The results of investigations on the average grain size, non-recrystallization rate, surface degree, hardness, punching processability, and heat deformation resistance of the steel sheet obtained by this method are shown in Table 1. The investigation items are as follows. The method described is determined. No. The average particle size of the fertilized iron is cut out from the steel sheet (rolling direction) After the grinding, the grain boundary of the ferrite is crystallized. 'A good microscope is observed at a magnification of _ times, and the photo is taken, and it is recorded in JIS G _ (attached instructions). The method for measuring the grain size of ferrite grains of the method steel (JIS G 〇 552 (1998) is calculated for the meaning D. The quasi-recrystallization rate is about the same as the average grain of the ferrite grain (four), and the direction of the ritual The thickness profile of the plate was observed at a magnification of 8 GG times. 'The area ratio of the non-recrystallization was determined, and this was taken as the rate of no recrystallization. 33 Surface roughness The arithmetic mean roughness was determined according to the measurement method specified in JIS B0601: ^ Hardness (HRB) ° The sample with a size of 2Gx6Gmm is cut from the steel plate and rided according to the Rockwell hard test method specified in JIS Z 2245. The fine B ruler is measured at ι〇, and the average value is taken as the hardness (HRB). Punching workability 098106119 200946696 by punching punching machine 'with punching size: inner diameter 14〇mmx outer diameter 16 〇 coffee, clearance: 10% of the thickness (thickness: 1.5 mm) punched Ring test piece, after which punching is performed on the rolled section of the steel sheet The end face was observed with an optical microscope at a magnification of 1 〇 to 2 〇, and evaluated according to the following criteria: * Good (〇): No cracks or voids on the end face of the punch, and no burrs or extreme depression occurred. Poor (X) cracks or holes on the punched end face: or burrs. Φ Heat resistance deformability For the same ring test piece as that of the punching processability evaluation, After that, it was made to be air-cooled, and the amount of warpage when the test piece reached room temperature was evaluated. The amount of the interesting piece was considered to be good as long as it was 01 mm or less. The measurement of the amount of facial curvature was carried out as follows. After heating and air-cooling, the test material is made on both sides by using the emery paper of #__, and the test material is placed on the pressure plate, and 10 points in the circumferential direction are measured using the contact height gauge. The height is determined by the difference between the thickness of the sheet produced by the micrometer and the maximum value is the amount of the curve. % 098106119 17 200946696
備註 1發明例1 1發明例1 發明例 1比較例I 比較例 比較例 發明例 紐曲量 (mm) g C3 S cd CD <=> g cd g o 沖孔加工性 〇 〇 〇 〇 〇 〇 〇 硬度 (HRB) 〇〇 CO 00 oo oo CO oo 表面粗度 (Ra : μπι) 0.20 C£5 r i o s ci oo CD 寸 <=> C<1 (Νϊ C5 s o 未再結晶率 (%> LO lo o LO LO S LO 寸 s 肥粒鐵平均粒徑 (#m) 寸 LO CO CO 卜 Ο oo 鋼成分（質量％) 0.225 0.213 0.238 0.175 0.192 0.156 0.211 0.005 0.004 0. 005 0.004 0.005 0. 004 0.005 r " < 0.035 0.038 0.041 0.037 0. 040 0.039 0.038 CO 0.004 0.007 0.008 0.010 0. 006 0. 009 0.008 CU 0. 020 0. 022 0.021 0.014 0.024 0.018 0.025 LTD 寸 Ο CO <〇 o 05 oa 〇· <=)· <zi o LO C5 0.007 0. 006 0.005 0.008 0.007 0.008 0.007 Ο 0.140 0.130 <=> LO 〇 Ο d g ι·*Η <z> ΙΛ r-H <=5 CO a <〇 M-h b〇 。女we缄駟頰长啭璲 200946696 如表1所示，可確認，任一發明例中的鋼板均獲得所需之肥 粒鐵平均粒徑、未再結晶率、表面粗度，且硬度（HRB)、沖孔 加工性以及耐熱變形性較優異。 _ [實施例2] 將具有表2所示之成分組成之鋼坯加熱至，之後， 以表3所示之加工溫度進行熱軋，且於鋼片輸送台上使其冷卻 後，以65(TC進行捲取。熱軋鋼板之板厚設成3〜1〇mm<j隨後， ® 利用酸洗除去鏽後，以50〜80%之範圍的軋縮率進行冷軋，製 成板厚為1. 5 mm之冷軋鋼板。將該冷軋鋼板脫脂之後，利用 連續退火爐進行退火。退火溫度設為68(TC以下之各種溫度， 退火時間為1分鐘。退火後，使鋼板以l(TC/s之速度冷卻， 之後，以320〜420。(：之溫度範圍内保溫2. 5分鐘，之後冷卻 至室溫。進而，利用調質軋壓線，以〇〜3. 5%之範圍内的軋縮 率（伸長率）於輕壓下進行軋製。 Ο 再者，表2所示之An變態點，係自各個鋼坯獲取測試片， 以1250°C持續加熱30分鐘，之後以rc/秒之冷卻速度進行冷 卻，利用示差熱膨脹計而進行測定。 以此所得之鋼板的肥粒鐵平均粒徑、未再結晶率、表面概 度、硬度（HRB)、沖孔加工性以及耐熱變形性的調查結果如表 3所示。 098106119 19 200946696 〔cvai (％®Η鉍) 備註 發明鋼 比較鋼 比較鋼 比較鋼 比較鋼 比較鋼 比較鋼 比較鋼 發明鋼 發明鋼 An變態點（°C) 寸 CO 〇〇 寸 (ΝΙ 〇〇 OJ LO oo C75 呀 OO οα oo oo LO 05 ΟΟ OO oo 05 oo H 寸 oo oo δ 0.225 <N1 CZ) 0.221 03 C3 [0.222 1 CO g C3 LTD oo r—H o 0.090 i 1 1 1 < <ΝΪ <=5 0.211 2： 0.005 s o C5 0.006 s Ο C=5 Ο Ο ο s 〇 <=> s o ai 0.005 S C=> o s o <35 > 14 0.035 (NI <=) 0.038 ΙΟ Ο CD CO g ο S ο o o 0. 038 oo s <=5 0.034 GO 0.004 s c=? d 0.003 1 0.006 1 0.005 g <=5 o o <=> 0.005 g C? CD 0.005 (2U 0.020 <=5 0.021 ο C=5 Οϊ <=) C3 0.025 寸 o o cJ LO S CD 0.025 LT3 寸 〇 <NI 〇* § ο 完 Ο 03 CO <=) σ> (N1 <=3 d s c=> CD 0.007 <=> o 0.400 CO ο CD c^> g ο 0.008 OO 〇 CZ5 0.009 0.007 | 0. 008 1 Ο 0.140 o oo ◦ <=> 寸 d ο CT> ¢=5 g czJ 0.006 <=> 0. 004 i—H <=> 0.085 鋼種 CQ CJ> Q W o sc 1—< ►—ϊ 。女WS^^IF长 < 竣«卜(拔 94 ο20 ° 〔£ Ψ1 C 備註c 發明例^ 發明例 比較例 發明例 比較例 比較例 比較例 比較例 發明例 比較例 比較例 比較例 比較例 峨例 比較例 比較例 發明例 I發明例1 勉曲量 (ram) «Ο s CD CD s G> 0.04 0.20 0.03 00 CM o s o 0.34 ! 0.18 CSJ 〇> 0.24 j s o s c> 5 O 1 0.06 沖孑L加 工性 〇 〇 X 〇 〇 X 〇 X 〇 X X X X X 〇 〇 〇 〇 (HRB) CO CO oo CO 0¾ CO oo 艺1 〇5 CO oo 〇o CO CO oo CO 00 Enl 到 SI oo CO 00 表面粗度 (Ra : //m) 0.20 CD CO t-H o C<1 寸 o 0.18 0.15 〇 o 0.48 CO CO o 05 03 〇 CO o IT3 1-H CO d 未再結晶率 (%) L〇 s CO] 051 § L〇| Ο 〇] oil LO in oo m oo § § Ol in 03 LDI g CO 00 肥粒鐵平均粒徑 (jum) 卜 寸 m Ο r-H 〇〇 Lrti CO CO 〇o 卜 ΙΟ cn 寸1 cal o i—1 COI CO Oi 調質札廢軋縮率 (伸長率)(%) 〇· CO LD CO o CO 〇 (Nl CO ιτ> CO o CO lO CO o OJ CO m CO ΙΛ CO ◦ CO c? CO <>3 CO CO o C5 CO ei ^ s CD s CD CD 另 CO 卜 导 CD o § s CO CO 另 CO s CD 导 CO § CO s CD 穿 CO g CO s CO s CD g ^ L〇 LT3 CD L£5 LTD L〇 CO s § L〇 0〇 o L〇 CO L〇 CO § o LO § LO lO oo §e 41 s Z〇 g § m o CO CD 另 CO s CO s C£) 穿 CO CO s CO s CD s CO s CO O LO CO CO § CO § LO g CO 熱軋加工溫度 CC) § 〇o S OO § oo s oo o CO oo s oo s 00 s oo s oo o LO 00 〇 00 o oo s 00 g 00 o CO oo § oo g oo o CO CO <>J CO CO c— oo 0¾ CO CO in 1 < 卜 ^ W -t； CQ O CJ? ta I—H t—Ϊ - 女瑞长<璲 6U901860 200946696 如表3所示，可確認，發明鋼即鋼種A、丨以及】中，當熱 軋時之加工溫度、冷軋時之軋縮率、退火溫度以及調質礼壓時 之軋縮率（伸長率）均處於適當範圍内時，可獲得所需之肥粒鐵 平均粒徑、未再結晶率以及表面粗度，且可獲得優良之硬度 (HRB)、沖孔加工性以及耐熱變形性。 與此相對，於比較鋼即鋼種B〜H中，即便熱軋時之加工溫 度、冷軋時之軋縮率、退火溫度均處於適當範圍内，肥粒鐵平 均粒徑、未再結晶率以及表面粗度中之任一者亦會處於適當範 ❹ 圍之外，結果，無法獲得本發明中所需之良好的硬度（HRB)、 沖孔加工性以及耐熱變形性。 再者，實施例1、2中，雖如下所述求出外觀上之未再結晶 率，但亦可獲得與以上述方式求出之外觀上之未再結晶率同等 的結果。 (外觀上之未再結晶率）=((HRB(p)) _Remark 1 Inventive Example 1 Inventive Example 1 Inventive Example 1 Comparative Example I Comparative Example Comparative Example Inventive Example New Curve Amount (mm) g C3 S cd CD <=> g cd go Punching Processability〇〇〇〇〇〇 〇 hardness (HRB) 〇〇CO 00 oo oo CO oo Surface roughness (Ra : μπι) 0.20 C£5 rios ci oo CD inch<=>C<1 (Νϊ C5 so no recrystallization rate (%> LO lo o LO LO S LO inch s Fertilizer iron average particle size (#m) inch LO CO CO dip oo steel composition (mass%) 0.225 0.213 0.238 0.175 0.192 0.156 0.211 0.005 0.004 0. 005 0.004 0.005 0. 004 0.005 r "< 0.035 0.038 0.041 0.037 0. 040 0.039 0.038 CO 0.004 0.007 0.008 0.010 0. 006 0. 009 0.008 CU 0. 020 0. 022 0.021 0.014 0.024 0.018 0.025 LTD inch Ο CO <〇o 05 oa 〇· <=)· <zi o LO C5 0.007 0. 006 0.005 0.008 0.007 0.008 0.007 Ο 0.140 0.130 <=> LO 〇Ο dg ι·*Η <z> ΙΛ rH <=5 CO a < 〇Mh b〇.Female we缄驷Cheek 啭璲200946696 As shown in Table 1, it can be confirmed that the steel sheets in any of the inventions have obtained the desired fertilizer granules. The iron average particle diameter, the non-recrystallization rate, the surface roughness, and the hardness (HRB), the punching workability, and the heat deformation resistance are excellent. _ [Example 2] The slab having the composition shown in Table 2 was heated to Then, hot rolling is performed at the processing temperature shown in Table 3, and after cooling on a steel sheet conveying table, coiling is performed at 65 (TC). The thickness of the hot-rolled steel sheet is set to 3 to 1 mm < j Then, after the rust is removed by pickling, cold rolling is performed at a rolling reduction ratio of 50 to 80% to obtain a cold-rolled steel sheet having a thickness of 1. 5 mm. After degreasing the cold-rolled steel sheet, continuous retreat is utilized. The furnace was annealed, and the annealing temperature was set to 68 (the temperature below TC, and the annealing time was 1 minute). After annealing, the steel sheet is cooled at a rate of 1 (TC/s, then 320 to 420. (: The temperature is kept for 2. 5 minutes, and then cooled to room temperature. Further, using a quenching and tempering line,轧~3. The rolling reduction (elongation) in the range of 5% is rolled under light pressure. Ο Furthermore, the An metamorphosis point shown in Table 2 is obtained from each billet at 1250 ° C. The heating was continued for 30 minutes, and then cooled at a cooling rate of rc/sec, and measured by a differential thermal dilatometer. The average particle diameter, non-recrystallization rate, surface roughness, hardness (HRB) of the obtained steel sheet. The results of the investigation of punching workability and heat deformation resistance are shown in Table 3. 098106119 19 200946696 [cvai (%®Η铋) Remarks Invented steel Comparative steel Comparative steel Comparative steel Comparative steel Comparative steel Comparative steel Comparative steel Invented steel Invention steel An metamorphic point (°C) inch CO 〇〇 inch (ΝΙ 〇〇OJ LO oo C75 呀 OO οα oo oo LO 05 ΟΟ OO oo 05 oo H inch oo oo δ 0.225 <N1 CZ) 0.221 03 C3 [0.222 1 CO g C3 LTD oo r—H o 0.090 i 1 1 1 <<ΝΪ<=5 0.211 2: 0.005 so C5 0.006 s Ο C=5 Ο Ο ο s 〇<=> so ai 0.005 SC=> oso <35 > 14 0.035 (NI <=) 0.038 ΙΟ Ο CD CO g ο S ο oo 0. 038 oo s <=5 0.034 GO 0.004 sc=? d 0.003 1 0.006 1 0.005 g <=5 oo <=> 0.005 g C? CD 0.005 (2U 0.020 <=5 0.021 ο C=5 Οϊ <=) C3 0.025 inch oo cJ LO S CD 0.025 LT3 inch 〇<NI 〇* § ο Ο CO 03 CO <=) σ> (N1 <=3 dsc=> CD 0.007 <=> o 0.400 CO ο CD c^> g ο 0.008 OO 〇CZ5 0.009 0.007 | 0. 008 1 Ο 0.140 o oo ◦ <=> inch d ο CT> ¢=5 g czJ 0.006 <=> 0 004 i—H <=> 0.085 Steel CQ CJ> QW o sc 1—< ►—ϊ. Female WS ^ ^ IF Length < 竣 卜 卜 拔 拔 C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C C EXAMPLES Comparative Example Comparative Example Inventive Example 1 Distortion amount (ram) «Ο s CD CD s G> 0.04 0.20 0.03 00 CM oso 0.34 ! 0.18 CSJ 〇> 0.24 jsos c> 5 O 1 0.06 孑 孑 L processing 〇〇X 〇〇X 〇X 〇XXXXX 〇〇〇〇(HRB) CO CO oo CO 03⁄4 CO oo Art 1 〇5 CO oo 〇o CO CO oo CO 00 Enl to SI oo CO 00 Surface roughness (Ra: //m) 0.20 CD CO tH o C<1 inch o 0.18 0.15 〇o 0.48 CO CO o 05 03 〇CO o IT3 1-H CO d No recrystallization rate (%) L〇s CO] 051 § L〇| LO 〇] oil LO in oo m oo § § Ol in 03 LDI g CO 00 Average grain size of ferrite iron (jum) 卜 inch m Ο rH 〇〇Lrti CO CO 〇o ΙΟ cn inch 1 cal oi-1 COI CO Oi quenching and tempering reduction rate (elongation) (%) 〇· CO LD CO o CO 〇(Nl CO ιτ> CO o CO lO CO o OJ CO m CO ΙΛ CO ◦ CO c? CO <>3 CO CO o C5 CO Ei ^ s CD s CD CD another CO CD CD o § s CO CO CO s CD 引 CO § CO s CD 穿 CO g CO s CO s CD g ^ L〇LT3 CD L£5 LTD L〇CO s § L〇0〇o L〇CO L〇CO § o LO § LO lO oo §e 41 s Z〇g § mo CO CD Additional CO s CO s C£) Wear CO CO s CO s CD s CO s CO O LO CO CO § CO § LO g CO Hot rolling processing temperature CC) § So S OO § oo s oo o CO oo s oo s 00 s oo s oo o LO 00 〇00 o oo s 00 g 00 o CO oo § oo g oo o CO CO <>J CO CO c- oo 03⁄4 CO CO in 1 < 卜^ W -t; CQ O CJ? ta I-H t-Ϊ - 女瑞长<璲6U901860 200946696 As shown in Fig. 3, it can be confirmed that in the invented steel, that is, the steel grades A, 丨 and 】, the processing temperature at the time of hot rolling, the rolling reduction at the time of cold rolling, the annealing temperature, and the rolling reduction (elongation) at the time of the tempering pressure When they are all in an appropriate range, the desired average grain size of the ferrite grains, the rate of non-recrystallization, and the surface roughness can be obtained, and excellent hardness (HRB), punching workability, and heat deformation resistance can be obtained. On the other hand, in the comparative steel, that is, the steel types B to H, even if the processing temperature during hot rolling, the rolling reduction ratio at the time of cold rolling, and the annealing temperature are within an appropriate range, the average grain size of the ferrite grains, the rate of non-recrystallization, and Any of the surface roughnesses may be outside the proper range, and as a result, good hardness (HRB), punching workability, and heat deformation resistance required in the present invention cannot be obtained. Further, in Examples 1 and 2, the unrecrystallized ratio in appearance was obtained as follows, but the same results as in the appearance of the unrecrystallized ratio obtained in the above manner were obtained. (No recrystallization rate in appearance) = ((HRB(p)) _
(HRB(S))’）/((HRB(H)) —(HRB(S))，）xlO〇«) O 其中， (HRB(P)):係具有部分再結晶組織之鋼板的洛氏硬度（β標 尺） (HRB(S))’ ：係完全成為再結晶組織之鋼板的洛氏硬度（β標 尺） Λ (HRB(H))’ ：係完全不含有再結晶組織之鋼板的洛氏硬度（Β 標尺） 098106119 22 200946696 又’（HRB(S))’與(HRB(H))，係以如下方式求得。將退火前之 冷軋鋼板於580°C及780°C加熱100秒以下之時間，之後，進 行水淬火，對於各個試料進行硬度（HRB)測定及組織觀察。對 • 於加熱溫度為580°C之試料’確認其完全不含再結晶組織後進 ' 行硬度（HRB)測定，作為（HRBOO)，。另一方面，對於加熱溫度 為7 8 0 °C之試料，確認其完全成為再結晶組織後進行硬度（H拙） 測定，作為（HRB(S))’。 ❹（產業上之可利用性） 根據本發明，藉由調整鋼成分後使鋼組織成為部分再結晶組 織’可獲付此較佳地適用於以離合片為首的汽車用變速器之 構成零件中之高強度（高硬度）且沖孔加工性以及耐熱變形性 優良的冷乳鋼板。根據本發明，冷軋後之退火可為未滿1小時 之短時間’而且能以生產效率極高之連續退火爐進行，故而， 本發明之冷軋鋼板的製造中不太會造成成本增多，從而能較佳 ❿ 地適用於價格競爭激烈之汽車零件中。 【圖式簡單說明】 圖 1 為表示 C*=(C%) + 〇. 15x(Mn%) + 0. 85x(P%)與硬度 (HRB)間之關係的圖表。 098106119 23(HRB(S))')/((HRB(H)) - (HRB(S)),)xlO〇«) O where (HRB(P)): Rockwell with steel plate with partially recrystallized structure Hardness (β scale) (HRB(S))' : Rockwell hardness (β scale) of steel sheet which is completely recrystallized (HRB(H))': Rockwell steel sheet which does not contain recrystallized structure at all Hardness (Β ruler) 098106119 22 200946696 Further, '(HRB(S))' and (HRB(H)) were obtained as follows. The cold-rolled steel sheet before annealing was heated at 580 ° C and 780 ° C for 100 seconds or less, and then water quenched, and hardness (HRB) measurement and microstructure observation were performed for each sample. For the sample "heating temperature of 580 °C", it was confirmed that it was completely free of recrystallized structure, and the hardness (HRB) was measured as (HRBOO). On the other hand, for the sample having a heating temperature of 780 °C, it was confirmed that the sample was completely recrystallized, and the hardness (H拙) was measured as (HRB(S))'. ❹ (Industrial Applicability) According to the present invention, the steel structure can be made into a partially recrystallized structure by adjusting the steel composition, which is preferably applied to the components of the automotive transmission including the clutch sheet. A cold-milk steel sheet excellent in high strength (high hardness) and excellent in punching workability and heat deformation resistance. According to the present invention, the annealing after the cold rolling can be performed for a short time of less than one hour, and can be carried out in a continuous annealing furnace having an extremely high production efficiency, so that the production of the cold-rolled steel sheet of the present invention is less likely to cause an increase in cost. Therefore, it can be preferably applied to automobile parts with high price competition. [Simple diagram of the diagram] Figure 1 is a graph showing the relationship between C*=(C%) + 〇. 15x(Mn%) + 0. 85x (P%) and hardness (HRB). 098106119 23