、發明說明： 【發明所屬之技術領域】 本發明疋有關於-種合金鋼材及其用途，特別是 種中碳合金鋼材及含有其之雙金制片。 a 【先前技術】 鐵瑞片多數是由高速㈣製成，高速鋼是藉由在 鐵碳合金中加入大量的鎢，並添加鉻、釩、鉬及結等元素 ’之後進行熱處理所製得。高速鋼耗具有較高硬度:高 ，600。。之切削溫度並適於高溫高速切削但是高速鋼的 初性較合金鋼或彈簧鋼為差，在高速切削或是切割硬質材 的過程中易產生彎曲或斷裂’此外，高速鋼所製成之鑛片 一般需要較高的製作成本，就屬於耗材的鋸片而言，將會 造成資源㈣f。近年來，在功能性及使料命的考量; 已研發出一種雙金屬鋸片（其型態包含鋸帶或圓孔鋸等）。 雙金屬雜片的結構包含一鋸齒以及一用於支撐鋸齒之 背材’其中，該鋸齒是由具有高硬度及適於高溫高速切削 之高迷鋼所製成，該背材是由具有良好韌性且不易斷裂之 合金鋼所f成，此雙金屬鋸片是利用真空電子束或雷射焊 接方式，將此兩種鋼材對銲在一起所製得，因而可完全保 留高速鋼及合金鋼的性質，同時可讓鋸片的使用性能以及 壽命得以提昇，也讓雙金屬鋸片成為市場主流。 叙用於製作鑛片背材之合金鋼的成分組成是由 ◎•25〜0.65 wt%之碳、2.0 wt%以下之矽、1.5 wt%以下之錳、 0.030 wt%以下之磷、〇.030 wt%以下之硫、i 5〇〜4 5〇糾％之 1379912 絡、L3.00 Wt%之箱，以及平衡量之鐵及雜質所構成。 雙金屬鑛片之合金鋼背材在熱處理過程中，需配合高速鋼 雜齒於讓Y進行真空淬火，再於，c進行長時間回火 ，然而以現有之碳素鋼或低合金鋼而言，尚無法滿足上述 熱處理及所需機械性質之要求，故做為背材^合金鋼首要 需具備高強度’才可與高速鋼鑛齒一同進行熱處理而不會 影響最終製得之雙金制片的性f。此外，在上述成分組 成中’雖然透過添加較多量的鉻及來提昇合金鋼的強度 及耐磨性能’但是在鑛切時，因背材需支㈣齒且所佔面 積較大’故需承受較多由抗切削力、衝擊與震動所造成之 下壓力’倘背材無法承受此極大的下壓力，將致使鑛片發 生刀口崩缺或折斷等情形。所以，除了高強度及对磨性能 之外，更希望能提昇背材的延勤#，以B及收此高壓震動下 所承受之衝擊能，進而提昇鋸片整體的使用壽命。 針對背材之延勃十生，一般是藉由？文變合金鋼之合金成 分組，及含量來提昇’在各合金成分中，已知當合金鋼含 有過量的硫時，由於硫為造成沿晶破壞的主要元素，也會 致使鋼材的延祕降低。而為了避免硫對㈣的影響，二 般會經由添加錳，使錳與硫結合形成硫化錳介在物，以減 少延性降低之機率。惟如此雖然可避免延性降低，但由於 硫化猛介在物呈條狀’仍可能損害合金鋼的勒性及其他機 械性質，因此需進-步控制介在物的形態（介在物較佳為球 狀）’才可有效提昇鋸片的整體性能。 此外若合金鋼可以具備良好延韌性，應有助於擴展 1379912 t 後續的應用，也就是除了做為鑛片的背材之外，還可用於 " 製作為其他工具，例如園藝剪等等。 . 由上述說明可知，現有合金鋼的性質仍有待提昇，特 別是延韌性的提昇，而此性質主要與合金鋼的成分組合及 含量有關，因此，如能找尋到更佳的合金成分組合及含量 範圍，應有助於提昇合金鋼的性質，更有助於擴展合金鋼 的後續應用。 【發明内容】 • 由於鋼材在製作過程中，通常需經過一連串的熱處理 步驟，而現有低合金鋼在熱處理後，尚無法滿足鋸片背材 所需之各項性質，更致使鋸片的使用壽命縮短，因此，本 案申請人針對此等缺失，開發新穎的合金成分組合，以製 得兼顧高強度及延韌性佳等性質之合金鋼材，並得以擴展 合金鋼的用途。 因此，本發明之目的，即在提供一種具有良好的抗拉 強度'靑曲性及撓性強度之中碳合金鋼材，此鋼材適用於 • 做為鋸片背材。 本發明之另一目的在於提供一種含有上述中碳合金鋼 材之雙金屬鋸片。 於是’本發明中碳合金鋼材以其之總重為i 〇〇 wt%計算 ，該鋼材係包含：0.4-0.7 Wt%的碳、2.0 wt%以下的矽、 0.2~2.0 wt%的猛、0.03 wt%以下的填、〇·〇3 wt%以下的硫、 0.1~1.5 wt%的鉻、0.1 〜〇·8 wt%的鉬、〇·〇ι~〇·2 wt%的飢、 一種或一種以上之輔助成分，平衡量的鐵及不顯著之雜質 5 其中，該辅助成分是選自於0.2 wt%以下的鈦、ο 2糾％以 下的鈮.或兩者之一組合。 :本發明之雙金屬鋸片包含一背材以及—與該背材結合 又置之尚速鋼鋸齒，該背材是由上述的中碳合金鋼材所製 传β 本發明之中碳合金鋼材由於添加有鈦、鈮或此兩者組 合之輔助成分，並同時控制其他成分的含量範圍，使合金 鋼材得以配合後續與高速鋼鋸齒結合後之高溫真空淬火及 長時間回火步驟，而在一連串熱處理後，該中碳合金鋼材 仍然可以具備良好的抗拉強度、彎曲性及撓性強度。 【實施方式】 較佳地’ s亥中碳合金鋼材包含：〇 45-0.7 wt%的碳、1 .〇 wt%以下的矽、0.5〜2.0 wt%的锰、〇.〇2 wt%以下的磷' 〇 〇2 wt%以下的硫、〇.5〜1.5 wt%的鉻、〇.1〜〇 6 wt%的鉬、 0.05〜0.2 wt%的釩、一種或一種以上之輔助成分，平衡量的 鐵及不顯著之雜質，其中，該輔助成分是選自於〇1糾％以 下的鈦、0.1 wt%以下的鈮或兩者之一組合；更佳地，該中 碳合金鋼材包含：0.45〜0.65 wt%的碳、0.25 wt%以下的碎 、0.5~i.6 wt%的錳、〇.〇2 wt%以下的磷 ' 0.005 wt%以下的 硫、0.9~1.1 wt%的絡、〇.3~〇.6 wt%的钥、〇.〇5~〇.l wt%的 釩、一種或一種以上之辅助成分，平衡量的鐵及不顯著之 雜質’其中’該辅助成分是選自於0.05 wt%以下的欽、〇.〇5 wt%以下的說或兩者之一組合。 上述提及的各個成分分別具有不同的作用，於本發明 1379912 - 中，除了碳'矽、錳、填、硫、鉻、鉬、釩及輔助成分為 •- 主要成分之外’其餘成分可依照實際需要再行添加。以下 . 將分別說明各種成分及其含量比例對於本發明之中碳合金 鋼材的影響： 碳：為鋼材中重要的強化元素，且於本發明中，碳是決定 碳化物析出的重要元素，當碳含量太低時，碳化物不 易生成，當碳含量太高時，則碳化物容易粗化，使得 鋼材強度太強’致使該鋼材的伸長率降低，所以本發 • 明的碳含量需控制在0.4~0.7 wt%。 矽.為固溶強化元素，矽可延遲雪明碳鐵的析出，使得過 飽和的碳得以產生大量碳化物析出。當添加不足時無 法得到上述效果’所以矽的最少添加量為0 01 wt%。 但添加過量會產生帶狀紅銹，影響外觀，故矽的上限 為 2.0 wt%。 錳：為鋼材中重要的固溶強化元素，於本發明中是用來提 鬲鋼材強度，但當猛含量高於2.〇 wt%時，會使鋼材的 0 成型性不佳。 填：屬於鋼材中的不純物，容易偏析至晶界，造成晶界脆 化，因此需將磷含量控制在〇.03 wt%以下，當磷含量 過高時，容易造成熱軋時的邊裂’且產品在使用時也 會產生脆性問題。 硫：屬於鋼材中的不純物，在高溫時可能產生Μ、邮而 與MnS，其巾’TiS、Ti4C2S2會消耗所添加的欽而 MnS受礼延後會呈長條狀’將成為破壞起始源，所以 7 硫含量需控制在0.03 wt%以下。 絡：為提高鋼材硬化能與提昇耐磨性的重要元素，同時也 是析出強化元素。在本發明中，當鉻含量高於15 wt% 時’將使鋼材強度顯著提昇，但韌性大幅下降；當絡 含量低於0.1 wt%時，則鋼材的強度將不足，且耐磨耗 性能將下降。 鉬：為析出強化與提高鋼材硬化能的重要元素，添加鉬可 有效減緩回火軟化的速度並阻止回火脆性的發生。在 本發明中，當鉬含量高於0.8 wt%時，將使鋼材強度與 抗回火軟化的速度顯著提昇，但細性大幅下降；當銦 含量低於0.1 wt%時，則鋼材的抗回火軟化與抗回火脆 性將不足，且硬化能將下降。所以其含量需控制在 〇· 1 ~0.8 wt%。 釩.為吊用的析出強化元素，當添加適量飢時，將可延後 TiC析出物的粗大，使得Tic可大量分散於肥粒鐵相中 。但是當釩含量太高時，也容易讓析出物粗化，所以 其含量需控制在〇.〇1〜0.2 wt%。 鈦為#用的析出強化元素，當添加〇.2 wt%以下之欽可產 生晶粒細化的效果，使鋼材強度與韌性同時提昇；但 疋田鈦3畺太咼時，易生成穩定的碳化物，對硬化能 不利’所以其含量需控制在0.2 wt%以下。 銳為*用的析出強化元素，當添加0.2 wt%以下之铌可產 生晶粒細化的效果，使鋼材強度與韌性同時提昇；但 疋备鈮含量太高時，將使得鋼材強度提昇，但韌性下 1379912 降，所以其含量需控制在0.2 wt%以下。[Technical Field] The present invention relates to an alloy steel material and a use thereof, particularly a medium carbon alloy steel material and a double gold sheet containing the same. a [Prior Art] Most of the Terry chips are made of high speed (four), which is obtained by heat-treating a large amount of tungsten in an iron-carbon alloy and adding elements such as chromium, vanadium, molybdenum and knots. High-speed steel consumption has a high hardness: high, 600. . The cutting temperature is suitable for high-temperature high-speed cutting, but the initiality of high-speed steel is worse than that of alloy steel or spring steel, and it is easy to bend or break during high-speed cutting or cutting of hard materials. In addition, the mine made of high-speed steel The film generally requires a higher production cost, and in the case of a saw blade that is a consumable, it will cause resources (four) f. In recent years, in terms of functionality and material considerations, a bi-metal saw blade (the type of which includes a saw band or a circular hole saw, etc.) has been developed. The structure of the bimetal strip comprises a saw tooth and a backing material for supporting the saw tooth. The saw tooth is made of high-strength steel with high hardness and high-speed cutting for high temperature, and the backing material is made of good toughness. And the alloy steel which is not easy to be broken is formed by using a vacuum electron beam or a laser welding method to weld the two steel materials together, thereby completely retaining the properties of the high speed steel and the alloy steel. At the same time, the performance and life of the saw blade can be improved, and the bimetal saw blade becomes the mainstream in the market. The composition of the alloy steel used to make the slab backing material is ◎•25~0.65 wt% carbon, 2.0 wt% or less, 1.5 wt% or less manganese, 0.030 wt% or less phosphorus, 〇.030 Sulphur below wt%, i 5〇~4 5〇% of 1379912, L3.00 Wt% box, and balance of iron and impurities. In the heat treatment process, the alloy steel backing of bimetal ore is required to be combined with high-speed steel teeth to allow Y to be vacuum quenched, and then c to be tempered for a long time, but in the case of existing carbon steel or low alloy steel. It is still unable to meet the above requirements of heat treatment and required mechanical properties. Therefore, as a backing material, alloy steel must first have high strength to be heat treated together with high speed steel ore without affecting the final double gold sheet. Sex f. In addition, in the above composition, 'while adding a large amount of chromium to improve the strength and wear resistance of the alloy steel', but in the case of the cut, because the backing material needs to support (four) teeth and occupy a large area, it is necessary to withstand More pressure caused by resistance to cutting forces, shocks and vibrations. 'If the backing material cannot withstand this extreme downforce, it will cause the cutting of the ore to break or break. Therefore, in addition to the high strength and the grinding performance, it is more desirable to enhance the extension of the backing material #, and to absorb the impact energy under the high pressure vibration, thereby improving the overall service life of the saw blade. For the end of the back of the material, it is generally by? Wenming alloy steel alloy composition group, and content to improve 'in each alloy composition, it is known that when the alloy steel contains excessive sulfur, the main element of the destruction of the crystal due to sulfur, will also cause the steel to reduce the mystery . In order to avoid the influence of sulfur on (4), manganese is added to the manganese to form a manganese sulfide intermediator by adding manganese to reduce the probability of ductility reduction. However, although the ductility can be avoided, the vulcanization is still in the form of strips, which may damage the alloying properties and other mechanical properties of the alloy steel. Therefore, it is necessary to further control the morphology of the medium (the medium is preferably spherical). 'In order to effectively improve the overall performance of the saw blade. In addition, if the alloy steel can have good ductility, it should help to expand the subsequent application of 1379912 t, that is, in addition to being used as a backing material for the ore sheet, it can also be used for other tools such as garden shears. It can be seen from the above description that the properties of the existing alloy steel still need to be improved, especially the improvement of the ductility, and this property is mainly related to the composition and content of the alloy steel. Therefore, if a better alloy composition and content can be found, The range should help to improve the properties of the alloy steel and help to extend the subsequent application of the alloy steel. [Summary of the Invention] • Since the steel is usually subjected to a series of heat treatment steps in the manufacturing process, the existing low alloy steel cannot meet the various properties required for the saw blade back material after heat treatment, and the service life of the saw blade is further improved. Shortened, therefore, the applicant of this case developed a novel alloy composition combination for these defects, in order to obtain alloy steel with high strength and good ductility, and to expand the use of alloy steel. Accordingly, it is an object of the present invention to provide a carbon alloy steel having a good tensile strength 'distortion and flexibility strength, which is suitable for use as a saw backing material. Another object of the present invention is to provide a bimetal saw blade comprising the above medium carbon alloy steel. Thus, the carbon alloy steel of the present invention is calculated based on the total weight of i 〇〇 wt%, which comprises: 0.4-0.7 Wt% of carbon, 2.0 wt% or less of bismuth, 0.2 to 2.0 wt% of violent, 0.03 Less than wt%, 〇·〇3 wt% sulfur, 0.1~1.5 wt% chromium, 0.1~〇·8 wt% molybdenum, 〇·〇ι~〇·2 wt% hunger, one or one The above auxiliary component, a balanced amount of iron and an insignificant impurity 5 wherein the auxiliary component is selected from the group consisting of titanium of 0.2 wt% or less, 铌 of 2 or less, or a combination of the two. The bimetal saw blade of the present invention comprises a backing material and a speed-speed steel sawtooth combined with the backing material, the backing material is produced by the above-mentioned medium carbon alloy steel material. The carbon alloy steel material in the invention is Adding an auxiliary component of titanium, niobium or a combination of the two, and simultaneously controlling the content range of other components, so that the alloy steel can be combined with the high-temperature vacuum quenching and long-term tempering step after the combination with the high-speed steel sawtooth, and in a series of heat treatment After that, the medium carbon alloy steel can still have good tensile strength, flexibility and flexibility. [Embodiment] Preferably, the carbon steel material of the s-sea includes: 〇45-0.7 wt% of carbon, 〇wt% or less of bismuth, 0.5-2.0 wt% of manganese, 〇.〇2 wt% or less Phosphorus 〇〇2 wt% or less of sulfur, 〇5 to 1.5 wt% of chromium, 〇1 to 〇6 wt% of molybdenum, 0.05 to 0.2 wt% of vanadium, one or more auxiliary components, balance amount Iron and insignificant impurities, wherein the auxiliary component is selected from the group consisting of titanium below 1%, 0.1 0.1% by weight or less, or a combination of the two; more preferably, the medium carbon alloy steel comprises: 0.45 ~0.65 wt% carbon, 0.25 wt% or less, 0.5 to i.6 wt% of manganese, 〇.〇2 wt% or less of phosphorus ' 0.005 wt% or less of sulfur, 0.9 to 1.1 wt% of ruthenium and osmium .3~〇.6 wt% key, 〇.〇5~〇.l wt% vanadium, one or more auxiliary components, balanced amount of iron and insignificant impurities 'where' the auxiliary ingredient is selected from It is less than 0.05 wt% of Qin, 〇. 〇 5 wt% or less or a combination of the two. Each of the above-mentioned components has a different function, and in the present invention 1379912 -, except for carbon '矽, manganese, fill, sulfur, chromium, molybdenum, vanadium and auxiliary components are - main components', the remaining components can be Actually need to add again. The following will explain the effects of various components and their content ratios on the carbon alloy steel in the present invention: Carbon: an important strengthening element in steel, and in the present invention, carbon is an important element determining carbide precipitation, when carbon When the content is too low, carbide is not easily formed. When the carbon content is too high, the carbide is easily coarsened, and the strength of the steel is too strong, so that the elongation of the steel is lowered, so the carbon content of the present invention needs to be controlled at 0.4. ~0.7 wt%.为. For the solid solution strengthening element, strontium can delay the precipitation of ferritic carbon iron, so that the supersaturated carbon can produce a large amount of carbide precipitation. When the addition is insufficient, the above effect cannot be obtained. Therefore, the minimum addition amount of hydrazine is 0 01 wt%. However, excessive addition will cause band red rust, which will affect the appearance. Therefore, the upper limit of bismuth is 2.0 wt%. Manganese: an important solid solution strengthening element in steel. It is used to improve the strength of steel in the present invention, but when the content is higher than 2. 〇 wt%, the formability of the steel is not good. Filling: It is an impurity in the steel, which is easy to segregate to the grain boundary, causing the grain boundary to become embrittled. Therefore, it is necessary to control the phosphorus content below 〇.03 wt%. When the phosphorus content is too high, it is easy to cause edge cracking during hot rolling. And the product will also have brittle problems when it is used. Sulfur: It is an impurity in steel. It may produce strontium, postal and MnS at high temperature. The towel 'TiS, Ti4C2S2 will consume the added MnS and the MnS will be elongated after the ceremony' will become the source of destruction. Therefore, the sulfur content of 7 should be controlled below 0.03 wt%. Network: An important element for improving the hardening energy of steel and improving wear resistance. It is also a strengthening element. In the present invention, when the chromium content is higher than 15 wt%, the steel strength will be remarkably improved, but the toughness is greatly decreased; when the content is less than 0.1 wt%, the strength of the steel will be insufficient, and the wear resistance will be decline. Molybdenum: an important element for precipitation strengthening and improving the hardening energy of steel. The addition of molybdenum can effectively slow down the temper softening and prevent the occurrence of temper brittleness. In the present invention, when the molybdenum content is higher than 0.8 wt%, the strength of the steel and the temper softening resistance are remarkably improved, but the fineness is drastically decreased; when the indium content is less than 0.1 wt%, the steel is resistant to back. Fire softening and tempering brittleness will be insufficient and hardening energy will decrease. Therefore, its content needs to be controlled at 〇·1 to 0.8 wt%. Vanadium. It is a precipitation strengthening element for hanging. When adding proper amount of hunger, the coarseness of TiC precipitates can be delayed, so that Tic can be dispersed in the ferrite iron phase in a large amount. However, when the vanadium content is too high, the precipitates are easily coarsened, so the content thereof should be controlled at 〜.〇1 to 0.2 wt%. Titanium is a precipitation strengthening element for #. When the addition of 〇.2 wt% or less, the effect of grain refinement is produced, and the strength and toughness of the steel are simultaneously improved. However, when the Titanium 3 is too ruthenium, it is easy to form stable carbonization. The substance is not good for hardening energy, so its content should be controlled below 0.2 wt%. The precipitation strengthening element used for sharpness* can increase the strength and toughness of the steel when the addition of 0.2 wt% or less, which will increase the strength and toughness of the steel. However, when the content of the ruthenium is too high, the strength of the steel will increase, but The toughness is 1379912, so its content should be controlled below 0.2 wt%.
較佳地，該中碳合金鋼材的顯微結構包含回火麻田散 • 鐵（於後文標示為「TM」）、回火變韌鐵（於後文標示為「TB j )、碳化物及球狀介在物，其中，該碳化物包含但不限於 (Fe，M)3C [該Μ是選自於鉻、鉬或此兩者之一組合]、Cr7C3 、M〇2C或此等之一組合，而該介在物包含但不限於硫化錳 。更佳地’該碳化物的平均粒徑範圍為2.0 μιη以下。 除了上述之必要成分之外，該中碳合金鋼材可選擇地 % 添加其他合金成分’較佳地，該中碳合金鋼材更包含 0.0005〜0_01 wt%之鈣，且鈣/硫之重量比範圍為$ 1 ;更佳 地’該鈣的含量範圍為0.0005〜〇 〇〇5 wt%。值得一提的是， 當鈣/硫重量比> 1時，該硫化錳介在物將呈現長條狀，並 散佈於回火麻田散鐵及回火變韌鐵之晶體内與晶界上，使 得晶體内與晶界上可能會形成裂縫，而容易產生内裂或發 生沿晶破裂的現象，但是當鈣/硫重量比$ !時，則會形成 球狀的介在物，並可避免在晶體内產生裂縫，或發生沿晶 • 破裂的現象，進而可藉此有效降低鋸切過程及彎曲成型之 彎裂或失效的機率。 較佳地，s亥中碳合金鋼材更包含j 〇 wt%以下的鋁更 佳地，該鋁的含量範圍為〇〇1〜〇〇6 wt%。添加鋁的主要目 的是在煉鋼時用來進行脫氧，當鋁含量低於〇〇1糾％時， 將造成脫氧不足，而當含量高於1〇 wt%時，可能會影響成 型十生0 較佳地，该肀碳合金鋼材更包含2〇 wt%以下之鎳；更 9 1379912 ㈣，該鎳之含量範料hG w咖τ。添加制主要作用 疋用來輔助韌性的提昇。 本發明之尹碳合金鋼材除了可做為雙金屬鑛片之背材 卜二由於其具有良好的抗拉強度、f曲性及撓性強度， b遇可製作成各種工具，例如園藝剪、板菁、对磨板、 石鑛月箄篝。 本發明之中碳合金鋼材的製備方式可依據習知煉鋼方 式製作，例如使含有前述合金成分組合及含量之鋼胚進行 熱軋、熱軋冷卻、盤捲、酸洗、退火、冷軋、退火再加工 、淬火冷卻、回火冷卻及冷卻步驟等，其中加工步驟可視 後續用途製作成不同形態。 本發明之雙金屬鑛片由於使用上述含有特定成分組合 的中碳合金鋼材做為背材’使得製備方式可完全依據習知 煉鋼方式製作’也就是分別製得待熱處理之合金鋼背材及 待？處理之高速鋼鋸齒，利用焊接方式將兩者予以接合， 接著再進行淬火、二次回火及冷卻步驟其中， 較佳可控制在麵⑽代，而回火溫度較佳可控制ς 450〜65〇。(：。 在上述製備步驟中，值得-提的是，該雙金屬鑛片之 合金鋼背材於淬火後具有特殊的顯微結構，即沃斯田鐵晶 粒尺寸小於50 pm，金相組織包含麻田散鐵及變韌鐵，以及 變韌鐵含量可達0.卜5%。此等顯微結構的產生是因為合金 鋼中含有鈦、鈮或此兩者之一組合’使得淬火後之沃斯田 鐵晶粒得以細化，更使得組織中的變韌鐵含量增加，而有 10 1379912 助於鋼材韌性的提昇。 較佳地，最後所製得之雙金屬鋸片之背材的顯微結構 包含回火麻田散鐵、回火變韌鐵、碳化物及球狀介在物， 其中，該碳化物包含但不限於（FeM)3C [該M是選自於鉻、 鉬或此兩者之一組合]、erf3、M〇2C或此等之一組合而 該介在物包含但不限於硫化錳。更佳地，該碳化物的平均 粒徑範圍為2.0 μιη以下。 本發明將就以下實施例來作進一步說明，但應瞭解的 是，該實施例僅為例示說明之用，而不應被解釋為本發明 實施之限制。 <實施例> [實施例1~8及比較例1〜5的共同製法] 首先，分別依據下表1所示之合金成分及含量，再分 別進行真空熔煉並連續鑄造而取得一中碳合金鋼胚，接著 分別依照下列（a)~(k)步驟進行製備： (a) 使所取付中奴合金鋼胚進行加熱並予以熱軋，完軋溫 度控制在950°C以下，以獲得一完軋鋼材； (b) 使該完軋鋼材進行層流冷卻； (c) 將該冷卻後的完軋鋼材於70〇°C以下的溫度進行盤捲 ，並獲得一鋼捲； (d) 以酸清洗鋼捲並去除其表面錄皮； (e) 使該酸洗後之鋼捲於700。(：以上的溫度進行退火處理 9 (f) 將該退火後之鋼捲進行冷軋； 11 (g) 將冷軋後之鋼捲進行退火處理以及再加工處理，得到 一待熱處理之合金鋼背材； (h) 利用焊接方式，將該合金鋼背材與一待熱處理之高速 鋼鋸齒予以接合，以獲得一待熱處理鋸片； (i) 使該待熱處理鋸片加熱至118〇〇C之溫度下進行淬火 冷卻，待冷卻至6〇。(：以下取出而得到一淬火鋸片。 以電子顯微鏡觀察所得之淬火鋸片的顯微結構，並利 用影像解析儀測量沃斯田鐵晶粒的尺寸及變韌鐵之含 量’所得結果如表2所示； (j) 使該淬火鋸片加熱到560<3C之溫度進行第一次回火冷 卻，待冷卻至1〇〇。(：以下，再進行以下步驟； (k) 重複步驟⑴進行第二次回火冷卻，得到一回火鋸片； 及 (l) 使該回火鋸片進行冷卻，即製得雙金屬鋸片。同樣以 電子顯微鏡觀察所得之雙金屬鋸片之背材部分的顯微 結構，並分析碳化物之成份及測量碳化物之粒徑所 得結果如表2所示。 [測試] 分別將實施例1〜8及比較例U所製得之雙金屬鋸片 進行以下測試，所得結果整理於表2令： 1. 抗拉強度（MPa):依據CNS 2U2G2〇14進行測試。目 刖業界對於鋸片之抗拉強度希望在1〇〇〇 Mpa以上。 2. 彎曲性：以V型塊彎曲試驗法進行測試。「◎」表示雙 金屬鋸片無彎裂及rx」表示雙金屬鋸片已彎裂。 12 1379912Preferably, the microstructure of the medium carbon alloy steel comprises tempered Ma Tian San • Iron (hereinafter referred to as “TM”), tempered toughened iron (hereinafter referred to as “TB j ), carbide and a spherical intervening substance, wherein the carbide includes, but is not limited to, (Fe, M) 3C [the cerium is selected from chromium, molybdenum or a combination of the two], Cr7C3, M〇2C or a combination thereof And the intermediate material includes, but is not limited to, manganese sulfide. More preferably, the average particle diameter of the carbide is in the range of 2.0 μm or less. In addition to the above-mentioned essential components, the medium carbon alloy steel may optionally add other alloy components. Preferably, the medium carbon alloy steel further comprises 0.0005 to 0_01 wt% of calcium, and the calcium/sulfur weight ratio ranges from $1; more preferably, the calcium content ranges from 0.0005 to 〇〇〇5 wt%. It is worth mentioning that when the calcium/sulfur weight ratio is > 1, the manganese sulfide mediator will be elongated and dispersed in the crystals and grain boundaries of the tempered granulated iron and tempered toughened iron. Therefore, cracks may form in the crystal and on the grain boundary, and it is prone to internal cracking or cracking along the crystal, but When the calcium/sulfur weight ratio is $, a spherical intervening material is formed, and cracks in the crystal or cracking along the crystal can be avoided, thereby effectively reducing the sawing process and bending molding. The probability of cracking or failure. Preferably, the carbon alloy steel in the shai further comprises less than j 〇 wt% of aluminum, and the content of the aluminum ranges from 〇〇1 to 〇〇6 wt%. The purpose is to carry out deoxidation during steel making. When the aluminum content is lower than 〇〇1%, it will cause insufficient deoxidation, and when the content is higher than 1〇wt%, it may affect the forming of the first generation. The niobium carbon alloy steel further comprises less than 2% by weight of nickel; further 9 1379912 (d), the content of the nickel is hG w τ. The main function of the addition is to assist in the improvement of toughness. In addition to being used as a backing material for bimetallic ore pellets, due to its good tensile strength, f-flexibility and flexibility, b can be made into various tools such as garden shears, sapphire, counter-grinding, stone. Mineral moon 箄篝. The preparation method of carbon alloy steel in the invention can be based on For the steelmaking method, for example, the steel preform containing the alloy composition combination and content is subjected to hot rolling, hot rolling cooling, coiling, pickling, annealing, cold rolling, annealing, refining, quenching cooling, tempering cooling, and cooling steps. The processing step can be made into different forms according to the subsequent use. The bimetallic ore piece of the present invention is made of the medium carbon alloy steel containing the specific component combination as the backing material, so that the preparation method can be completely made according to the conventional steel making method. That is, the alloy steel backing material to be heat-treated and the high-speed steel sawtooth to be processed are separately prepared, and the two are joined by welding, and then quenching, secondary tempering and cooling steps are performed, preferably in the surface (10) generation. The tempering temperature is preferably controlled to ς 450~65〇. (: In the above preparation steps, it is worth mentioning that the alloy steel backing of the bimetallic ore has a special microstructure after quenching, that is, the Worthite iron grain size is less than 50 pm, and the metallographic structure contains the Ma Tian. The iron and toughened iron, as well as the toughening iron content can reach 0. 5%. These microstructures are produced because the alloy steel contains titanium, niobium or a combination of the two to make the warhead after quenching The grain size of the field iron is refined, and the content of toughened iron in the structure is increased, and 10 1379912 contributes to the improvement of the toughness of the steel. Preferably, the microstructure of the backing of the bimetal saw blade finally obtained includes Fire Ma Tian loose iron, tempered toughened iron, carbide and spherical mediator, wherein the carbide includes but is not limited to (FeM) 3C [The M is selected from chromium, molybdenum or a combination of the two] And erf3, M〇2C or a combination thereof, and the inclusions include, but are not limited to, manganese sulfide. More preferably, the average particle size of the carbides is in the range of 2.0 μηη or less. The present invention will further Description, but it should be understood that this embodiment is merely illustrative It is not to be construed as limiting the practice of the invention. <Examples> [Common methods of Examples 1 to 8 and Comparative Examples 1 to 5] First, the alloy compositions shown in Table 1 below and The content is then vacuum smelted and continuously cast to obtain a medium carbon alloy steel embryo, and then prepared according to the following steps (a) to (k): (a) heating and heating the extracted slave steel. Rolling, finishing temperature is controlled below 950 °C to obtain a finished steel; (b) laminar cooling of the finished steel; (c) cooling of the finished steel below 70 °C The temperature is coiled and a steel coil is obtained; (d) the steel coil is cleaned with acid and the surface is removed; (e) the pickled steel coil is rolled at 700. (: The above temperature is annealed 9 ( f) cold-rolling the annealed steel coil; 11 (g) annealing and re-treating the cold-rolled steel coil to obtain an alloy steel backing material to be heat-treated; (h) by means of welding The alloy steel backing is joined with a high speed steel sawtooth to be heat treated to obtain a heat treatment saw (i) The saw blade to be heat treated is heated to a temperature of 118 ° C for quenching and cooling, and is cooled to 6 〇. (: The following is taken out to obtain a quench saw blade. The obtained quench saw blade is observed by an electron microscope. The microstructure was measured and the size of the iron grain of the Worthfield and the content of the toughened iron were measured by an image analyzer. The results are shown in Table 2; (j) The quench saw blade was heated to a temperature of 560 < 3 C for the first time. Tempering and cooling, to be cooled to 1 〇〇. (: The following steps are performed; (k) repeating step (1) for the second tempering to obtain a tempering saw blade; and (l) making the tempering blade After cooling, a bimetal saw blade was obtained. The microstructure of the back part of the obtained bimetal saw blade was also observed by an electron microscope, and the composition of the carbide and the particle size of the carbide were analyzed. Show. [Test] The bimetal saw blades prepared in Examples 1 to 8 and Comparative Example U were subjected to the following tests, and the results were summarized in Table 2: 1. Tensile strength (MPa): Tested according to CNS 2U2G2〇14 . It is expected that the tensile strength of the saw blade is above 1 〇〇〇 Mpa. 2. Flexibility: Tested by the V-block bending test method. "◎" means that the bi-metal saw blade has no crack and rx" means that the bi-metal saw blade has been bent. 12 1379912
3. 撓性強度：將雙金屬鋸片在外徑60 mm之試桿上捲繞 36(Γ，當雙金屬鋸片展平恢復原狀後，觀察是否產生傷 痕或裂紋，「◎」表示雙金屬鋸片無裂紋及「X」表示 雙金屬鋸片有裂紋。 13 13799123. Flexural strength: Wind the bi-metal saw blade on the test rod with an outer diameter of 60 mm (Γ, when the bi-metal saw blade is flattened and restored to its original shape, observe whether there is a flaw or crack, “◎” indicates a double metal saw The film has no cracks and the "X" indicates that the bimetal saw blade has cracks. 13 1379912
熱處理後之背材的顯微結構 Xi + £3 荽 + ·£> m Η .+ Η TM+TB+石炭化物+球狀介在物 TM+TB+碳化物+球狀介在物 TM+TB+碳化物+球狀介在物 TM+TB+碳彳匕物+球狀介在物 TM+TB+碳化物+球狀介在物 TM+TB+石炭化物+球狀介在物 TM+TB+碳彳匕物+球狀介在物 P +碳化物+球狀介在物 TM+碳化物+球狀介在物 TM+碳化物+球狀介在物 TM+碳化物+球狀介在物 ΤΜ+碳化物+球狀介在物 黎 ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ 未測試 X X ◎ ◎ 雙金屬 鋸片之 彎曲性 ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ 未測試 X X X X 躁4茗 轉笔g ‘ W $ 制π漶 1 1172.5 1280.4 1492.5 1464.1 1371.7 1448.8 1242.5 1486.3 912.5 1087.3 1246.5 | 1394.8 1455.6 4<夺_ vn oi 〇\ CN 卜 m 00 (N m m (N m (N 〇 〇 〇 〇 〇 改要 無趣 C3 PQ + ca M+B M+B M+B M+B M+B M+B M+B CQ Oh •^田t έ ^ 4 | 本W吨w 46.8 IT) 寸 43.2 42.4 1> 寸 41.6 47.5 v〇 寸 無法偵測 117.5 121.0 1 ί 125.8 184.1 CN m 寸 1〇 v〇 00 CN m 寸 { K ' 蓉: 。賴qY饽嫦「龚蛘^劣镑」 ^•tnllF^IAI^luKIAiJb^r#^^ 丨 W 泳 qi^uNOIAI , 」，黎屆翱^0桕< 长啭「d」w ,f蔬 UJTU二♦凜丨W%嗒与嘁頌，途 「OQ1」，黎趄田璲¥0长啭「PMH」 翱长<「3」，1^田璲长^「1^ •q •ϋ I3.79912„ -·* · 一· r; -w.厂‘. .· -> ·» [結果] 由表2之結果可發現，以三種機械性質來看，比較例 2~5之雙金屬鋸片的彎曲性皆不佳，且比較例2及3的撓 性強度也不佳，抗拉強度範圍在912.5〜1455.6 MPa;反觀 本案之實施例1~8，彎曲性及撓性強度都非常良好，而抗 拉強度範圍為1172·5~1492·5 MPa，稍高於比較例2~5之抗 拉強度範圍’由此可證明實施例1〜8具有較佳之性質。 再比對表1之成分組成及含量，可發現比較例2~5並 未添加鈦、鈮或此兩者之組合，導致合金鋼材的彎曲性皆 不佳，且比較例2及3的撓性強度也不佳，由此可見，添 加鈦、鈮或此兩者之組合確實有效提昇彎曲性及撓性強度 ，以及可讓抗拉強度符合需求。需注意的是，比較例4及 5之背材是因為添加較多的鎳才可具有良好的撓性強度， 但其背材之彎曲性仍無法符合要求。 再就月材之顯微結構而言，相較於實施例^，比較 厂！ 1 5 &未發現有逢物鐵的存在，另外，比較例2〜$於泮 火後之背材的沃斯田鐵晶粒尺寸皆大於10 0 μ m，再由最後 所製知X金屬鑛片之背材部分的顯微結構來看，可發現比 較例1〜5都未產生回火變勒鐵。顯見實施例u之合金成 ^合及含量已讓背材在熱處理後的顯微結構產生新額的 。 受韌鐵確實有效地讓背材的韌性提昇 在實施例1〜8之昔分* ^ 材中，經電子顯微鏡的觀察，發現 顯1。構中之兔化物的平均粒握範圍為2.〇_以下。 16Microstructure of heat treated backing material Xi + £3 荽+ ·£> m Η .+ Η TM+TB+Carbide + spheroidal TM+TB+carbide+spherical TM+TB+carbide+ Spherical medium TM+TB+carbonium+spherical TM+TB+carbide+spherical TM+TB+carboniferous+spherical TM+TB+carbonium+spherical P+ Carbide + spheroidal TM + carbide + spheroidal TM + carbide + spheroidal TM + carbide + spheroidal ΤΜ + carbide + spheroidal mediated ◎ ◎ ◎ ◎ ◎ ◎ ◎ ◎ Test XX ◎ ◎ Bending property of bimetal saw blade ◎ ◎ ◎ ◎ ◎ ◎ ◎ Not tested XXXX 躁 4茗 Transfer pen g ' W $ system 漶 漶 1 1172.5 1280.4 1492.5 1464.1 1371.7 1448.8 1242.5 1486.3 912.5 1087.3 1246.5 | 1394.8 1455.6 4<夺 _ vn oi 〇\ CN 卜 m 00 (N mm (N m (N tampering to be boring C3 PQ + ca M+B M+B M+B M+B M+B M+B M +B CQ Oh •^田t έ ^ 4 | Ben W ton w 46.8 IT) inch 43.2 42.4 1> inch 41.6 47.5 v inch cannot detect 117.5 121.0 1 ί 125.8 184.1 CN m inch 1〇v〇 00 CN m 寸{ K ' 蓉: 赖qY饽嫦 "龚蛘^劣磅" ^•tnllF^IAI^luKIAiJb^r#^^ 丨W swimming qi^uNOIAI , ", 黎届翱^0桕< Long 啭 "d" w, f vegetable UJTU 2 ♦ 凛丨 W% 嗒 and 嘁颂, way "OQ1", Li 趄 璲 璲 ¥ 0 long 啭 "PMH" 翱 long < "3", 1 ^ 田璲长 ^ " 1^ •q •ϋ I3.79912„ -·* · 一·r; -w.厂'. .· -> ·» [Results] From the results of Table 2, it can be found from three mechanical properties. The bimetal saw blades of Examples 2 to 5 were not excellent in flexibility, and the flexural strengths of Comparative Examples 2 and 3 were not good, and the tensile strength ranged from 912.5 to 1455.6 MPa; in contrast, Examples 1 to 8 of the present case, bending Both the properties and the flexural strength are very good, and the tensile strength ranges from 1172·5 to 1492·5 MPa, which is slightly higher than the tensile strength range of Comparative Examples 2 to 5, thus it can be proved that Examples 1 to 8 are preferable. nature. Further, comparing the composition and content of Table 1, it was found that Comparative Examples 2 to 5 did not add titanium, niobium or a combination of the two, resulting in poor bendability of the alloy steel and flexibility of Comparative Examples 2 and 3. The strength is also not good, so it can be seen that the addition of titanium, niobium or a combination of the two is effective to improve the flexibility and flexibility, and the tensile strength can meet the demand. It should be noted that the backing materials of Comparative Examples 4 and 5 have good flexural strength because of the addition of more nickel, but the bending property of the backing material still fails to meet the requirements. In terms of the microstructure of the moon, compared to the example ^, compare the factory! 1 5 & No existence of iron found in the object, in addition, Comparative Example 2 ~ $ after the bonfire of the back of the Worthfield iron grain size is greater than 10 0 μ m, and then the final known X metal ore In view of the microstructure of the backing portion, it was found that Comparative Examples 1 to 5 did not produce tempering. It is apparent that the alloying and content of the alloy of Example u has resulted in a new amount of microstructure of the backing material after heat treatment. The toughness of the iron is effective to improve the toughness of the backing material. In the first and second parts of Examples 1 to 8, it was found by electron microscopy. The average grain holding range of the rabbit compound in the structure is 2. 〇 _ or less. 16