TWI384077B - Anti-tempering softening treatment of high-carbon tool steel and its manufacturing method - Google Patents
Anti-tempering softening treatment of high-carbon tool steel and its manufacturing method Download PDFInfo
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Description
本發明是有關於一種高碳工具鋼，特別是指一種抗回火軟化處理的高碳工具鋼及其製造方法。The present invention relates to a high carbon tool steel, and more particularly to a high carbon tool steel resistant to temper softening and a method of manufacturing the same.
一般用於工具產品使用的鋼材需具備有高硬度及耐磨耗的性質，而具有這樣的性質且價格便宜的材料又以高碳工具鋼最受業界使用，而用於園藝花卉剪裁的工具產品多半以高碳工具鋼所製，且為了使工具產品擁有美觀的表面、潤滑基件及耐銹蝕的功能，會在工具鋼的表面施予表面處理，而該表面處理的溫度通常約為300℃。The steels generally used for tool products need to have high hardness and wear resistance. The materials with such properties and low price are the most used in the industry for high carbon tool steel, and the tool products for gardening flower cutting. Mostly made of high-carbon tool steel, and in order to make the tool product have an attractive surface, lubricating base and rust-resistant function, the surface treatment of the tool steel is applied, and the surface treatment temperature is usually about 300 ° C. .
從冶金學來看，當高碳工具鋼在300℃進行一段時間的加熱處理，就相當於使該工具鋼進行了一次回火處理(Tempering)，因此，在學理上，會造成高碳工具鋼的硬度降低，且發生軟化的現象。From the perspective of metallurgy, when the high carbon tool steel is heated at 300 ° C for a period of time, it is equivalent to a tempering of the tool steel. Therefore, it is theoretically high carbon steel. The hardness is lowered and softening occurs.
為了避免工具鋼的硬度下降，添加適當的合金元素，和施予適當的熱處理，就成為業者研究的方向。In order to avoid the hardness reduction of the tool steel, the addition of appropriate alloying elements, and the application of appropriate heat treatment, has become the direction of the research.
例如日本特開2006-63384發明專利案所揭露的「具有高衝擊強度的高碳鋼及其製造方法」，其高碳鋼包含：0.60~1.30質量%的碳、1.0質量%以下的矽、0.2~1.5質量%的錳、0.02質量%以下的磷、0.02質量%以下的硫，以及平衡量的鐵及不顯著之雜質，且如上經由淬火和回火處理之高碳鋼中未溶解的碳化物之體機率(Vf)需滿足8.5<15.3×15.3的碳含量-Vf<10.0的方程式，而其製造方法是將一鋼材 在760~850℃之間加熱，並持溫3~30分鐘，然後進行急冷至室溫~200℃之間，再次加熱至150~350℃之間，持溫10~180分鐘，得到平均粒徑不小於1.0μm的碳化物。For example, "high carbon steel having high impact strength and a method for producing the same" disclosed in Japanese Laid-Open Patent Publication No. 2006-63384, the high carbon steel includes: 0.60 to 1.30% by mass of carbon, 1.0% by mass or less of niobium, 0.2. ~1.5% by mass of manganese, 0.02% by mass or less of phosphorus, 0.02% by mass or less of sulfur, and a balance of iron and insignificant impurities, and undissolved carbides in high carbon steel treated by quenching and tempering as above The body probability (Vf) needs to satisfy the equation of 8.5 < 15.3 × 15.3 carbon content - Vf < 10.0, and the manufacturing method is to use a steel Heat between 760~850 °C, hold the temperature for 3~30 minutes, then quench to room temperature ~200 °C, reheat to 150~350 °C, hold the temperature for 10~180 minutes, get the average particle size Carbide not less than 1.0 μm.
這樣的方式，雖然提高了高碳工具鋼的耐衝擊性，也提高了硬度和韌性，並使該工具鋼在顯微組織下得到微小的等軸相晶粒，但是，對於該體積率的計算方式顯得模糊不清，難以執行，且在接近300℃的加熱方式，容易引起低溫回火的脆性產生，而使得此項專利在實際生產過程中有不易操作的問題。In this way, although the impact resistance of the high carbon tool steel is improved, the hardness and toughness are also improved, and the tool steel is obtained with a small equiaxed phase grain under the microstructure, but the calculation of the volume ratio is performed. The method is ambiguous and difficult to perform, and the heating method close to 300 °C easily causes the brittleness of low-temperature tempering, which makes the patent difficult to operate in the actual production process.
因此，本發明之目的，即在提供一種能夠維持彎曲性，且維持硬度或使硬度上升的抗回火軟化的高碳工具鋼及其製造方法。Accordingly, an object of the present invention is to provide a high-carbon tool steel which is capable of maintaining flexibility and maintaining hardness or increasing hardness, and a method for producing the same.
於是，本發明之抗回火軟化處理的高碳工具鋼，以其總重量之百分比為100wt%計算，該工具鋼的組成成份包含0.50~1.10wt%的碳、2.0wt%以下的矽、0.20~2.0wt%的錳、0.030wt%以下的磷、0.030wt%以下的硫、2.0wt%以下的鋁、0.0005~0.0100wt%的鈣、0.3~1wt%的合金元素、平衡量的鐵，以及不顯著之雜質，其中，鈣的重量百分比對硫的重量百分比之比值小於1，且該合金元素是選自於鉻、鉬，及此等之組合。另外，該工具鋼的顯微結構包含有呈板狀之低碳麻田散鐵Therefore, the temper softening-treated high carbon tool steel of the present invention is calculated as a percentage of the total weight of 100% by weight, and the composition of the tool steel comprises 0.50 to 1.10 wt% of carbon, 2.0 wt% or less of bismuth, 0.20. ~2.0 wt% of manganese, 0.030 wt% or less of phosphorus, 0.030 wt% or less of sulfur, 2.0 wt% or less of aluminum, 0.0005 to 0.0100 wt% of calcium, 0.3 to 1 wt% of an alloying element, a balance of iron, and An insignificant impurity wherein the ratio by weight of calcium to the weight percent of sulfur is less than 1, and the alloying element is selected from the group consisting of chromium, molybdenum, and the like. In addition, the microstructure of the tool steel comprises a plate-shaped low-carbon 麻田散铁
本發明之抗回火軟化處理的高碳工具鋼的製造方法，包含一熱軋步驟、一熱軋冷卻步驟、一盤捲步驟、一酸洗 步驟、一退火步驟、一淬火步驟、一第一回火步驟、一第二回火步驟、一表面處理步驟，及一冷卻步驟。The method for manufacturing the temper softening-treated high carbon tool steel of the present invention comprises a hot rolling step, a hot rolling cooling step, a coiling step, and a pickling a step, an annealing step, a quenching step, a first tempering step, a second tempering step, a surface treatment step, and a cooling step.
該熱軋步驟是將上述之組成成份的鋼材加熱後，進行熱軋，得到一完軋鋼材。In the hot rolling step, the steel material having the above composition is heated and then hot rolled to obtain a rolled steel material.
該熱軋冷卻步驟是將該完軋鋼材進行冷卻。The hot rolling cooling step is to cool the finished steel material.
該盤捲步驟是以不大於700℃的捲取溫度對經過該冷卻步驟的該完軋鋼材進行盤捲，得到一鋼捲。The coiling step coils the finished steel material subjected to the cooling step at a coiling temperature of not more than 700 ° C to obtain a steel coil.
該酸洗步驟是去除該鋼捲表面銹皮。The pickling step is to remove the surface scale of the coil.
該退火步驟是將經過該酸洗步驟的鋼捲以不小於700℃進行退火處理後，進行再加工處理，得到一待加工的鋼片。In the annealing step, the steel coil subjected to the pickling step is annealed at not less than 700 ° C, and then subjected to reprocessing to obtain a steel sheet to be processed.
該淬火步驟是將該鋼片加熱至780℃~880℃後，進行淬火冷卻，得到一淬火鋼片。In the quenching step, the steel sheet is heated to 780 ° C to 880 ° C and then quenched to obtain a quenched steel sheet.
該第一次回火步驟是將該淬火鋼片加熱至不小於300℃後，進行冷卻，得到一待回火鋼片。The first tempering step is to heat the quenched steel sheet to not less than 300 ° C and then to obtain a steel sheet to be tempered.
該第二次回火步驟是將該待回火鋼片加熱至不小於300℃後，進行冷卻，得到一回火鋼片。The second tempering step is to heat the steel sheet to be tempered to not less than 300 ° C, and then to obtain a tempered steel sheet.
該表面處理步驟是將該回火鋼片加熱至不小於300℃，並在該回火鋼片表面進行一鍍膜處理。The surface treatment step is to heat the tempered steel sheet to not less than 300 ° C and perform a coating treatment on the surface of the tempered steel sheet.
該冷卻步驟是將完成表面處理步驟的該回火鋼片進行冷卻，並得到一高碳工具鋼。The cooling step is to cool the tempered steel sheet that has completed the surface treatment step and obtain a high carbon tool steel.
本發明之功效在於：控制高碳工具鋼的組成成份中鈣對硫的重量百分比值小於1，並添加0.3~1wt%合金元素，該合金元素選自於鉻、鉬，及此等之組合，並在其製造過 程中，利用該第一次回火步驟和該第二次回火步驟，使上述的合金元素能抑制碳從麻田散鐵組織中擴散出來與細小碳化物以分散硬化的方式分佈，在顯微組織結構中得到硬度高的低碳麻田散鐵、(Fe,M)3 C型碳化物和球狀介在物，其中，M代表鉻或鉬，如此，能保有該高碳工具鋼整體的硬度，更佳地可使其硬度上升，且同時保有整體的彎曲性。The effect of the invention is to control the composition of the high carbon tool steel to have a weight percentage of calcium to sulfur of less than 1, and to add 0.3 to 1 wt% of an alloying element selected from the group consisting of chromium, molybdenum, and the like. And in the manufacturing process, the first tempering step and the second tempering step are utilized to prevent the above-mentioned alloying elements from inhibiting the diffusion of carbon from the granulated iron structure and the distribution of the fine carbides in a dispersed hardening manner. In the microstructure, low-carbon ramie loose iron, (Fe, M) 3 C-type carbide and spherical intercalation are obtained, wherein M represents chromium or molybdenum, so that the high carbon tool steel can be retained as a whole. The hardness is more preferably increased in hardness while maintaining overall flexibility.
有關本發明之前述及其他技術內容、特點與功效，在以下配合參考圖式之二個較佳實施例的詳細說明中，將可清楚的呈現。The above and other technical contents, features and advantages of the present invention will be apparent from the following detailed description of the preferred embodiments of the invention.
在本發明被詳細描述之前，要注意的是，在以下的說明中，類似的元件是以相同的編號來表示。Before the present invention is described in detail, it is noted that in the following description, like elements are denoted by the same reference numerals.
本發明抗回火軟化處理的高碳工具鋼之第一較佳實施例，以總重量之百分比為100wt%計算，該工具鋼的組成成份包含0.87wt%的碳、0.20wt%的矽、0.40wt%的錳、0.011wt%的磷、0.006wt%的硫、0.035wt%的鋁、0.001wt%的鈣、0.36wt%的合金元素、平衡量的鐵，以及不顯著之雜質，其中，鈣的重量百分比對硫的重量百分比之比值為0.16，該比值遠小於1，且在本實施例中該合金元素為0.15wt%的鉻、0.21wt%的鉬。A first preferred embodiment of the temper softening treated high carbon tool steel of the present invention, calculated as a percentage by weight of 100 wt%, the tool steel composition comprising 0.87 wt% carbon, 0.20 wt% bismuth, 0.40 Wt% manganese, 0.011 wt% phosphorus, 0.006 wt% sulfur, 0.035 wt% aluminum, 0.001 wt% calcium, 0.36 wt% alloying elements, balanced amount of iron, and insignificant impurities, of which calcium The ratio of the weight percentage to the weight percentage of sulfur is 0.16, which is much less than 1, and in the present embodiment the alloying element is 0.15 wt% chromium and 0.21 wt% molybdenum.
上述提及的各個成份分別具有不同的作用，於本發明中，除了碳、矽、錳、磷、硫及鋁為煉鋼過程中的主要成份之外，還包含了改善機械性質的鈣、鉻及鉬，而其餘的 成份可依據實際需要進行添加，由於這些其餘的成份並非為本實施例討論的重點，故不在此詳加說明。以下是針對本實施例中提及的各種成分及其含量比例對於本發明之高碳工具鋼的影響：碳：為工具鋼中重要的強化元素，也是決定碳化物析出的重要元素，當碳含量太低時，會使碳化物不易析出，當碳含量過高時，使得該工具鋼的伸長率降低，韌性下降，所以本發明的碳含量需控制在0.5~1.10 wt%，在本實施例中碳含量為0.87wt%。Each of the above-mentioned components has different functions. In the present invention, in addition to carbon, bismuth, manganese, phosphorus, sulfur and aluminum, which are main components in the steelmaking process, calcium and chromium are also included to improve mechanical properties. And molybdenum, while the rest The ingredients can be added according to actual needs. Since these remaining ingredients are not the focus of the discussion in this example, they are not described in detail here. The following are the effects of the various components mentioned in the examples and their proportions on the high carbon tool steel of the present invention: carbon: an important strengthening element in tool steel, and an important element in determining carbide precipitation, when carbon content When the temperature is too low, the carbide is not easily precipitated. When the carbon content is too high, the elongation of the tool steel is lowered and the toughness is lowered. Therefore, the carbon content of the present invention is controlled to be 0.5 to 1.10 wt%, in this embodiment. The carbon content was 0.87 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與合金元素析出結合，產生大量奈米級的析出物，但當矽添加不足時無法得到上述效果，又添加過量時會產生帶狀紅銹，影響外觀，故在本發明中是以2.0wt%為上限，在本實施例中矽含量為0.20wt%。矽: It is a solid solution strengthening element, which delays the precipitation of ferritic carbon iron, so that supersaturated carbon can be combined with alloying elements to produce a large number of nano-scale precipitates. However, when the strontium is insufficiently added, the above effects cannot be obtained. When the addition is excessive, banding red rust is generated, which affects the appearance. Therefore, in the present invention, the upper limit is 2.0% by weight, and in the present embodiment, the cerium content is 0.20% by weight.
錳：為工具鋼中重要的固溶強化元素，在本發明中是用來提高工具鋼的強度，但當錳含量太高時，會使工具鋼的成型性不佳，故在本發明中是以0.40wt%為上限，在本實施例中錳含量為0.4wt%。Manganese: an important solid solution strengthening element in tool steel. It is used to improve the strength of tool steel in the present invention, but when the manganese content is too high, the formability of the tool steel is not good, so in the present invention The upper limit is 0.40% by weight, and the manganese content in this embodiment is 0.4% by weight.
磷：屬於鋼材中的不純物，容易在晶界上產生偏析，引發晶粒脆裂，且當磷含量過高時，容易造成熱軋時的邊裂，因此需將磷含量控制在0.030wt%以下，在本實施例中磷含量為0.011wt%。Phosphorus: It is an impurity in steel, which is easy to segregate on the grain boundary and cause grain brittleness. When the phosphorus content is too high, it is easy to cause edge cracking during hot rolling. Therefore, the phosphorus content should be controlled below 0.030wt%. In the present embodiment, the phosphorus content is 0.011% by weight.
硫：屬於鋼材中的不純物，在高溫時可能產生硫化錳，而 硫化錳受軋延後會呈長條狀，成為破壞起始源，所以硫含量需控制在0.03wt%以下，在本實施例中硫含量為0.006wt%。Sulfur: It is an impurity in steel, which may produce manganese sulfide at high temperatures. The manganese sulfide is elongated after being rolled and becomes the source of destruction, so the sulfur content needs to be controlled to 0.03 wt% or less, and the sulfur content in this embodiment is 0.006 wt%.
鋁：主要是用來幫助煉鋼過程中，進行脫氧過程，當鋁含量太低將造成脫氧不易，而當含量過高時，將影響成型性，在本發明中是控制在2.0wt%以下，在本實施例中鋁含量為0.035wt%。Aluminum: It is mainly used to help the deoxidation process during the steel making process. When the aluminum content is too low, the deoxidation is not easy, and when the content is too high, the moldability will be affected. In the present invention, the control is below 2.0 wt%. In the present embodiment, the aluminum content was 0.035 wt%.
鈣：與硫的親和性佳，可與硫形成硫化鈣，取代硫化錳生成，能在晶界中控制介在物的成長，故在本發明中控制在0.0005~0.0100wt%，在本實施例中鈣含量為0.001wt%。Calcium: has good affinity with sulfur, can form calcium sulfide with sulfur, replaces the formation of manganese sulfide, and can control the growth of the medium in the grain boundary, so it is controlled in the present invention at 0.0005 to 0.0100% by weight, in this embodiment The calcium content was 0.001% by weight.
鉻：為提高工具鋼的硬化能與提昇耐磨性的重要元素，同時也是碳化物形成元素，可以降低回火軟化程度，故在本發明中控制在0.1~0.5wt%，在本實施例中鉻含量為0.15wt%。Chromium: In order to improve the hardening energy of the tool steel and the important element for improving the wear resistance, and also the carbide forming element, the temper softening degree can be lowered, so it is controlled in the present invention in the range of 0.1 to 0.5 wt%, in this embodiment. The chromium content was 0.15 wt%.
鉬：為提高工具鋼硬化能與析出強化的元素，同時在回火時可阻止麻田散鐵中碳的擴散，可有效減緩回火軟化的速度，故在本發明中控制在0.1~0.5wt%，在本實施例中鉬含量為0.21wt%。Molybdenum: In order to improve the hardening energy and precipitation strengthening of the tool steel, it can prevent the diffusion of carbon in the granulated iron in the tempering, and can effectively slow down the temper softening speed. Therefore, in the present invention, the control is 0.1-0.5 wt%. In the present embodiment, the molybdenum content was 0.21% by weight.
參閱圖1，該高碳工具鋼的製造方法依序包含一熱軋步驟11、一熱軋冷卻步驟12、一盤捲步驟13、一酸洗步驟14、一退火步驟15、一淬火步驟16、一第一次回火步驟17、一第二次回火步驟18、一表面處理步驟19，及一冷卻步驟20。Referring to FIG. 1 , the manufacturing method of the high carbon tool steel includes a hot rolling step 11 , a hot rolling cooling step 12 , a coiling step 13 , a pickling step 14 , an annealing step 15 , and a quenching step 16 . A first tempering step 17, a second tempering step 18, a surface treatment step 19, and a cooling step 20.
該熱軋步驟11是將具有上述之組成成份的鋼材加熱後，運用一般軋延機進行熱軋，並得到一完軋鋼材。In the hot rolling step 11, the steel material having the above composition is heated, and then hot rolled by a general rolling mill to obtain a finished steel material.
該熱軋冷卻步驟12是將該完軋鋼材，以層流方式，進行冷卻。The hot rolling cooling step 12 is to cool the steel material by laminar flow.
該盤捲步驟13是以700℃以下的捲取溫度，經過該冷卻步驟20的該完軋鋼材進行盤捲，得到一鋼捲，在本實施例中該捲取溫度是660℃。The coiling step 13 is coiling at the coiling temperature of 700 ° C or lower, and the rolled steel material passing through the cooling step 20 is coiled to obtain a steel coil. In the present embodiment, the coiling temperature is 660 ° C.
該酸洗步驟14是將該鋼捲以進行酸洗，用以去除該鋼捲表面銹皮。The pickling step 14 is to pickle the steel coil to remove scale on the surface of the coil.
該退火步驟15是將經過該酸洗步驟14的鋼捲以不小於700℃進行退火處理，進行再加工處理，得到一待加工的鋼片，本步驟是用來消除該鋼捲在該熱軋步驟11中所形成的應力，在本實施例中該退火溫度是740℃。The annealing step 15 is to anneal the steel coil passing through the pickling step 14 at not less than 700 ° C for reprocessing to obtain a steel sheet to be processed. This step is for eliminating the steel coil in the hot rolling. The stress formed in the step 11 is 740 ° C in the present embodiment.
搭配參閱圖2，該淬火步驟16是將該鋼片加熱至810℃，並持溫30分鐘，使碳及合金元素能充份固溶於沃斯田鐵中，然後在15分鐘內，在油中，淬火冷卻至30℃的室溫，得到一淬火鋼片，該淬火鋼片的顯微組織為硬度很高的高碳麻田散鐵。沃斯田鐵在淬火冷卻過程中，在通過麻田散鐵的生成溫度200℃時，開始變態生成板狀及條狀的麻田散鐵，麻田散鐵是工具鋼中硬度最高的金相組織，故存在大量的麻田散鐵，是工具鋼必備的基本條件。Referring to FIG. 2, the quenching step 16 is to heat the steel sheet to 810 ° C and hold the temperature for 30 minutes to fully dissolve the carbon and alloying elements in the Worthite iron, and then in the oil in 15 minutes, After quenching and cooling to room temperature of 30 ° C, a quenched steel sheet having a microstructure of high-hardness numb loose iron having a high hardness is obtained. During the quenching and cooling process, the Worthite iron began to metamorphose into the plate-like and strip-shaped granulated iron in the temperature of 200 °C. The granulated iron is the hardest metallographic structure in the tool steel. There are a large number of granulated irons, which are essential for tool steel.
該第一次回火步驟17是將該淬火鋼片加熱至310℃後，持溫30分鐘後，在15分鐘內，透過保護性氣體氣冷的方式，冷卻至30℃的室溫，得到一待回火鋼片。在此步驟 鉻、鉬及此等之組合的合金元素，能抑制碳從高碳麻田散鐵擴散出來的速度，使麻田散鐵仍能保持其正方性，故可維持整體高硬度。In the first tempering step 17, after heating the quenched steel sheet to 310 ° C, the temperature is maintained for 30 minutes, and then cooled to a room temperature of 30 ° C by means of a protective gas gas cooling in 15 minutes. Steel sheet to be tempered. In this step Chromium, molybdenum and alloying elements of these combinations can inhibit the diffusion of carbon from the high-carbon hemp field, so that the granulated iron can maintain its squareness, thus maintaining the overall high hardness.
該第二次回火步驟18是將該待回火鋼片加熱至310℃後，持溫280分鐘後，在15分鐘內，以透過保護性氣體氣冷的方式，進行冷卻，得到一回火鋼片。在此步驟是使高碳麻田散鐵轉變成低碳麻田散鐵及(Fe,M)3 C碳化物，同時合金元素亦能阻擋碳化物的成核及成長，使碳化物在高溫回火仍能保持均勻分布的細小顆粒，得到平均粒徑1.0μm以下的碳化物。The second tempering step 18 is to heat the steel sheet to be tempered to 310 ° C, hold the temperature for 280 minutes, and then cool it by means of a protective gas gas cooling in 15 minutes to obtain a tempered steel. sheet. In this step, the high-carbon ramification iron is converted into low-carbon ramification iron and (Fe,M) 3 C carbide, and the alloying elements can also block the nucleation and growth of the carbide, so that the carbide is tempered at high temperature. The fine particles which are uniformly distributed can be obtained to obtain a carbide having an average particle diameter of 1.0 μm or less.
在此一提的是，當鈣的重量百分比對硫的重量百分比的比值不小於1時，硫化錳會散佈形成於麻田散鐵晶體內與晶界上且呈長條狀的介在物，然而，長條狀的介在物提供裂縫在晶體內與兩晶界上生長的適當途徑，而容易產生內裂或發生沿晶破裂的現象，但當鈣的重量百分比對硫的重量百分比的比值小於1時，可形成球狀複合型的介在物。如此，可避免在晶體內產生裂縫，或發生沿晶破裂的現象，進而，藉此有效降低彎曲成形時的加工破裂機會，將完成此步驟的回火鋼片進行硬度值測試，得到硬度值為HRC 54.1。Herein, when the ratio of the weight percentage of calcium to the weight percentage of sulfur is not less than 1, manganese sulfide is dispersed in a matrix formed in the crystal of the granulated iron and in the form of a strip, however, The long strip-like medium provides a suitable way for cracks to grow in the crystal and on both grain boundaries, and is prone to internal cracking or crystal cracking, but when the ratio of the weight percentage of calcium to the weight percentage of sulfur is less than one It can form a spherical composite type of intervening substance. In this way, it is possible to avoid the occurrence of cracks in the crystal or the phenomenon of cracking along the crystal, thereby further reducing the chance of processing cracking during bending forming, and performing the hardness value test on the tempered steel sheet which has completed this step to obtain a hardness value. HRC 54.1.
該表面處理步驟19是將該回火鋼片，進行噴砂處理後，加熱至300℃，並在該回火鋼片表面進行10分鐘的鐵氟龍塗覆，但也可在噴砂處理後，採用蒸鍍法在該回火鋼片表面進行氮化鈦蒸鍍，而這些表面處理為所屬技術領域者 熟知的技術，故在此不再繼續說明。The surface treatment step 19 is that the tempered steel sheet is subjected to sand blasting, heated to 300 ° C, and subjected to Teflon coating on the surface of the tempered steel sheet for 10 minutes, but may also be used after sand blasting. The vapor deposition method performs titanium nitride vapor deposition on the surface of the tempered steel sheet, and these surface treatments are known to those skilled in the art. Well-known techniques, so the description will not be continued here.
該冷卻步驟20是將完成表面處理步驟19的該回火鋼片以空冷的方式進行冷卻，並得到一高碳工具鋼，將完成此步驟的高碳工具鋼片進行硬度值測試，得到硬度值為HRC 55.2，與完成第二次回火步驟18的回火鋼胚比較，硬度值確實有顯著的上升。The cooling step 20 is to cool the tempered steel sheet which has completed the surface treatment step 19 by air cooling, and obtain a high carbon tool steel. The high carbon tool steel sheet which has completed this step is subjected to a hardness test to obtain a hardness value. For HRC 55.2, there is a significant increase in the hardness value compared to the tempered steel blank that completed the second tempering step 18.
如上所述，本實施例的該高碳工具鋼利用鈣的重量百分比對硫的重量百分比之比值小於1，和0.3~1wt%的合金元素(選自於鉻、鉬，及其組合)，並經過第一次和第二次回火步驟17、18後，能有效的得到低碳麻田散鐵以及分散硬化的(Fe,M)3 C碳化物，使整體硬度提升，避免回火後產生的軟化現象，且能避免介在物形成長條狀，並降低介在物的長寬比，減少在晶體內與晶界上有破裂的現象發生。As described above, the high carbon tool steel of the present embodiment utilizes a ratio of the weight percentage of calcium to the weight percentage of sulfur of less than 1, and 0.3 to 1 wt% of an alloying element (selected from chromium, molybdenum, and combinations thereof), and After the first and second tempering steps 17, 18, the low-carbon ramification iron and the dispersion-hardened (Fe,M) 3 C carbide can be effectively obtained to improve the overall hardness and avoid the softening after tempering. Phenomenon, and can avoid the formation of long strips in the intervening substance, and reduce the aspect ratio of the intervening material, and reduce the occurrence of cracks in the crystal and the grain boundary.
本發明高碳工具鋼的製造方法之第二較佳實施例，大致上是與該第一較佳實施例相同，其中不相同之處在於：一第一次回火步驟17、一第二次回火步驟18，及一表面處理步驟19。The second preferred embodiment of the method for manufacturing high carbon tool steel of the present invention is substantially the same as the first preferred embodiment, wherein the difference is that: a first tempering step 17, a second time back Fire step 18, and a surface treatment step 19.
參閱圖3，該第一次回火步驟17是將該淬火鋼片加熱至350℃後，持溫480分鐘後，在15分鐘內，透過保護性氣體氣冷，冷卻至30℃的室溫，得到一待回火鋼片。Referring to FIG. 3, the first tempering step 17 is to heat the quenched steel sheet to 350 ° C, hold the temperature for 480 minutes, and then air-cooled through a protective gas for 15 minutes to cool to a room temperature of 30 ° C. Get a steel sheet to be tempered.
該第二次回火步驟18是將該待回火鋼片加熱至350℃後，持溫480分鐘後，在15分鐘內，透過保護性氣體進行冷卻，得到一回火鋼片，該回火鋼片得到硬度值為HRC 55.59。The second tempering step 18 is to heat the steel sheet to be tempered to 350 ° C, hold the temperature for 480 minutes, and then cool it through a protective gas in 15 minutes to obtain a tempered steel sheet. The sheet obtained a hardness value of HRC 55.59.
該表面處理步驟19是將該回火鋼片，進行噴砂處理後，加熱至310℃，並在該回火鋼片表面進行10分鐘的鐵氟龍塗覆。The surface treatment step 19 is that the tempered steel sheet is subjected to sand blasting, heated to 310 ° C, and subjected to Teflon coating on the surface of the tempered steel sheet for 10 minutes.
將經過該表面處理步驟19和冷卻步驟20的高碳工具鋼進行硬度值的測量，得到硬度值為55.11，雖略有下降，但下降幅度並不大，仍為一般業者能使用的範圍內。The high carbon tool steel subjected to the surface treatment step 19 and the cooling step 20 was subjected to measurement of the hardness value to obtain a hardness value of 55.11. Although the pressure was slightly decreased, the decrease was not large, and it was still within the range usable by the general practitioner.
將上述的第一實施例之製造方法，以不同成份的實驗例和多個比較例和習知進行比對，得到表一中每一鋼種的成份分佈及表二中每一鋼種的機械性質：
在表一中顯示，習知1是不添加鉻和鉬，也不添加鈣；習知2是添加0.15wt%的鉻，不添加鈣和鉬；習知3是添加0.16wt%的鉻，但不添加鈣和鉬，習知1的組成成份在此是作為一基準比較值，用來作本發明鈣、鉻和鉬的條件比 對。It is shown in Table 1 that conventional 1 does not add chromium and molybdenum, and does not add calcium; conventionally, 2 adds 0.15 wt% of chromium without adding calcium and molybdenum; conventionally, 3 adds 0.16 wt% of chromium, but Without adding calcium and molybdenum, the composition of the conventional one is used here as a reference comparison value for the condition ratio of calcium, chromium and molybdenum of the present invention. Correct.
比較例1是添加0.002wt%的鈣，且添加0.15wt%的鉻，但不添加鉬，其鈣的重量百分比對硫的重量百分比之比值為0.33，該值小於1，但鉻含量與鉬含量之總添加量小於0.3wt%；比較例2是添加0.008wt%的鈣，且添加0.15wt%的鉻，及添加0.2wt%的鉬，其鈣的重量百分比對硫的重量百分比之比值為1.14，該值大於1。Comparative Example 1 was to add 0.002 wt% of calcium and add 0.15 wt% of chromium, but without adding molybdenum, the ratio of the weight percentage of calcium to the weight percentage of sulfur was 0.33, which was less than 1, but the chromium content and molybdenum content. The total addition amount is less than 0.3% by weight; Comparative Example 2 is adding 0.008% by weight of calcium, and adding 0.15% by weight of chromium, and adding 0.2% by weight of molybdenum, the ratio of the weight percentage of calcium to the weight percentage of sulfur is 1.14. , the value is greater than 1.
實驗例1是添加0.001wt%的鈣，且添加0.15wt%的鉻，並添加0.21wt%的鉬，其鈣的重量百分比對硫的重量百分比之比值為0.16，該值小於1，鉻含量與鉬含量之總添加量為0.36wt%；實驗例2是添加0.001wt%的鈣，且不添加鉻，但添加0.4wt%的鉬，其鈣的重量百分比對硫的重量百分比之比值為0.14，該值小於1，鉻含量與鉬含量之總添加量為0.4wt%；實驗例3是添加0.003wt%的鈣，且添加0.15wt%的鉻，並添加0.20wt%的鉬，其鈣的重量百分比對硫的重量百分比之比值為0.42，該值小於1，鉻含量與鉬含量之總添加量為0.35wt%。Experimental Example 1 was to add 0.001 wt% of calcium, and add 0.15 wt% of chromium, and add 0.21 wt% of molybdenum, the ratio of the weight percentage of calcium to the weight percentage of sulfur was 0.16, the value was less than 1, and the chromium content was The total addition amount of molybdenum content was 0.36 wt%; Experimental Example 2 was to add 0.001 wt% of calcium without adding chromium, but adding 0.4 wt% of molybdenum, the ratio of the weight percentage of calcium to the weight percentage of sulfur was 0.14. The value is less than 1, and the total addition amount of the chromium content and the molybdenum content is 0.4 wt%; Experimental Example 3 is to add 0.003 wt% of calcium, and add 0.15 wt% of chromium, and add 0.20 wt% of molybdenum, the weight of the calcium The ratio of the percentage by weight to sulfur is 0.42, which is less than 1, and the total addition of the chromium content to the molybdenum content is 0.35 wt%.
參閱表二，為依照表一的工具鋼組成成份，並以本發明的製造方法實施後，進行機械性質測試：
藉由表二可以得知，以表一所列的各組成份利用本發明抗回火軟化處理的高碳工具鋼之製造方法進行時，在經 過表面處理步驟19後，習知1~2和比較例1的硬度值，皆低於工具鋼基本要求的硬度(HRC50±2)，而習知1~3和比較例1的硬度值皆呈現下降，顯示不但硬度值過低，且有回火軟化的現象，而其抗回火軟化的增加量也都明顯的過低，並呈現負值。而從顯微組織的觀察中得到，習知1和比較例1，在顯微組織內並沒有硬度高的麻田散鐵的存在，只有硬度低的波來鐵和球狀介在物存在，因此，導致整體的硬度過低，故在彎曲試驗時，呈現無彎曲裂痕的狀態。It can be known from Table 2 that when the components listed in Table 1 are used in the method for producing high carbon tool steel which is resistant to temper softening treatment of the present invention, After the surface treatment step 19, the hardness values of the conventional 1 to 2 and the comparative example 1 are lower than the hardness required by the tool steel (HRC 50 ± 2), and the hardness values of the conventional 1 to 3 and the comparative example 1 are both presented. The decrease shows that not only the hardness value is too low, but also the phenomenon of temper softening, and the increase in anti-temper softening is also too low and exhibits a negative value. From the observation of the microstructure, in the conventional example 1 and the comparative example 1, there is no presence of the high-density granulated iron in the microstructure, and only the low-hardness of the ferritic iron and the globular intermediate exist, therefore, As a result, the hardness of the whole is too low, so that in the bending test, there is no state of bending cracks.
相較於習知1~3和比較例1，將比較例2和本發明之實驗例1~3利用本發明抗回火軟化處理的高碳工具鋼之製造方法進行，且在經過表面處理步驟19後，顯現比較例2和本發明之實驗例1~3的硬度值皆大於工具鋼基本要求的硬度(HRC50±2)，且其抗回火軟化的增加量也都有明顯增加，並呈現正值，而本發明的實驗例1~3的顯微組織則分佈著硬度高的低碳麻田散鐵組織，和分散硬化的(Fe,M)3 C型的碳化物，及提高韌性的球狀介在物，因此，在作彎曲試驗時，還能保有原來的高硬度，並具有良好的彎曲性質，但是，在該比較例2中鈣重量百分比對硫重量百分比的比值為1.14，該比值大於1，使得該比較例2的顯微組織內有長條狀的介在物產生，因此，容易發生晶體內與晶界的破裂現象，導致彎曲性下降，容易形成彎裂。Compared with the conventional examples 1 to 3 and the comparative example 1, the comparative example 2 and the experimental examples 1 to 3 of the present invention were carried out by the method for producing high-carbon tool steel which is resistant to temper softening treatment of the present invention, and subjected to a surface treatment step. After 19, the hardness values of Comparative Example 2 and Experimental Examples 1 to 3 of the present invention were all greater than the hardness required by the tool steel (HRC 50 ± 2), and the increase in the anti-temper softening was also significantly increased. Positive values, and the microstructures of Experimental Examples 1 to 3 of the present invention are distributed with a low-hardness ramadrite iron structure having high hardness, and a dispersion-hardened (Fe, M) 3 C-type carbide, and a ball for improving toughness. It is in the form of a material. Therefore, it can retain the original high hardness and have good bending properties when subjected to the bending test. However, in Comparative Example 2, the ratio of the weight percentage of calcium to the weight percentage of sulfur is 1.14, and the ratio is larger than 1. In the microstructure of Comparative Example 2, a long interlaminar substance was generated in the microstructure. Therefore, cracking in the crystal and the grain boundary easily occurred, and the bendability was lowered, and the crack was easily formed.
歸納上述，本發明之抗回火軟化處理的高碳工具鋼，利用鈣的重量百分比對硫的重量百分比之比值不大於1，並 添加0.3~1wt%合金元素為鉻、鉬，及此等之組合，並在其製造過程中，利用該第一次回火步驟17和該第二次回火步驟18，使該合金元素能抑制碳從麻田散鐵組織中擴散出來.與細小碳化物以分散硬化的方式分佈，在顯微組織結構中得到硬度高的低碳麻田散鐵、(Fe,M)3 C型碳化物和球狀介在物，如此能保有該高碳工具鋼整體的硬度，更佳地，可使其硬度值上升，且同時保有整體的彎曲性，故確實能達到本發明之目的。In summary, the temper softening-treated high carbon tool steel of the present invention utilizes a ratio of the weight percentage of calcium to the weight percentage of sulfur of not more than 1, and adds 0.3 to 1 wt% of the alloying elements to chromium, molybdenum, and the like. Combining, and during its manufacture, utilizing the first tempering step 17 and the second tempering step 18, the alloying element inhibits the diffusion of carbon from the granulated iron structure. The fine carbides are dispersed and hardened. Distribution of low-carbon ramie loose iron, (Fe, M) 3 C-type carbide and spherical intercalation in the microstructure, which can maintain the overall hardness of the high-carbon tool steel, preferably The ground can be increased in hardness and at the same time retains overall flexibility, so that the object of the present invention can be achieved.
惟以上所述者，僅為本發明之較佳實施例而已，當不能以此限定本發明實施之範圍，即大凡依本發明申請專利範圍及發明說明內容所作之簡單的等效變化與修飾，皆仍屬本發明專利涵蓋之範圍內。The above is only the preferred embodiment of the present invention, and the scope of the invention is not limited thereto, that is, the simple equivalent changes and modifications made by the scope of the invention and the description of the invention are All remain within the scope of the invention patent.
11‧‧‧熱軋步驟11‧‧‧ hot rolling steps
12‧‧‧熱軋冷卻步驟12‧‧‧ hot rolling cooling steps
13‧‧‧盤捲步驟13‧‧‧ coiling steps
14‧‧‧酸洗步驟14‧‧‧ Pickling step
15‧‧‧退火步驟15‧‧‧ Annealing step
16‧‧‧淬火步驟16‧‧‧Quenching steps
17‧‧‧第一次回火步驟17‧‧‧First tempering step
18‧‧‧第二次回火步驟18‧‧‧Second tempering step
19‧‧‧表面處理步驟19‧‧‧ Surface treatment steps
20‧‧‧冷卻步驟20‧‧‧Cooling step
圖1是一流程圖，說明本發明抗回火軟化處理的高碳工具鋼之製造方法；圖2是一曲線圖，說明本發明抗回火軟化處理的高碳工具鋼之製造方法的第一較佳實施例，且說明該淬火步驟到該第二次回火的溫度時間關係；及圖3是一曲線圖，說明本發明抗回火軟化處理的高碳工具鋼之製造方法的第二較佳實施例，且說明該淬火步驟到冷卻步驟的溫度時間關係。1 is a flow chart illustrating a method of manufacturing a high carbon tool steel resistant to temper softening treatment of the present invention; and FIG. 2 is a graph illustrating the first method of manufacturing a high carbon tool steel resistant to temper softening treatment of the present invention. a preferred embodiment, and illustrating the temperature time relationship of the quenching step to the second tempering; and FIG. 3 is a graph illustrating a second preferred method of manufacturing the temper softening resistant high carbon tool steel of the present invention. Embodiments, and illustrate the temperature time relationship of the quenching step to the cooling step.
11‧‧‧熱軋步驟11‧‧‧ hot rolling steps
12‧‧‧熱軋冷卻步驟12‧‧‧ hot rolling cooling steps
13‧‧‧盤捲步驟13‧‧‧ coiling steps
14‧‧‧酸洗步驟14‧‧‧ Pickling step
15‧‧‧退火步驟15‧‧‧ Annealing step
16‧‧‧淬火步驟16‧‧‧Quenching steps
17‧‧‧第一次回火步驟17‧‧‧First tempering step
18‧‧‧第二次回火步驟18‧‧‧Second tempering step
19‧‧‧表面處理步驟19‧‧‧ Surface treatment steps
20‧‧‧冷卻步驟20‧‧‧Cooling step
Claims (10)
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| TW97137721A TWI384077B (en) | 2008-10-01 | 2008-10-01 | Anti-tempering softening treatment of high-carbon tool steel and its manufacturing method |
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| TW97137721A TWI384077B (en) | 2008-10-01 | 2008-10-01 | Anti-tempering softening treatment of high-carbon tool steel and its manufacturing method |
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| Publication Number | Publication Date |
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| TW201014916A TW201014916A (en) | 2010-04-16 |
| TWI384077B true TWI384077B (en) | 2013-02-01 |
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| TWI276690B (en) * | 2003-09-29 | 2007-03-21 | Jfe Steel Corp | Steel product for induction hardening, induction hardened member using the same, and manufacturing methods therefor |
| TWI294917B (en) * | 2004-03-10 | 2008-03-21 | Jfe Steel Corp | High carbon hot-rolled steel sheet and method for manufacturing the same |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| TWI276690B (en) * | 2003-09-29 | 2007-03-21 | Jfe Steel Corp | Steel product for induction hardening, induction hardened member using the same, and manufacturing methods therefor |
| TWI294917B (en) * | 2004-03-10 | 2008-03-21 | Jfe Steel Corp | High carbon hot-rolled steel sheet and method for manufacturing the same |
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| Publication number | Publication date |
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| TW201014916A (en) | 2010-04-16 |
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