TW202142706A - Stainless steel sheet, method for producing same, edged tools and cutlery - Google Patents
Stainless steel sheet, method for producing same, edged tools and cutlery Download PDFInfo
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Abstract
Description
本發明係關於一種具有較高之硬度及良好之表面品質之不鏽鋼鋼板,其適合用於菜刀或剪刀、醫療用手術刀等切削用具、餐桌用之刀或叉、匙等刀具、及鑷子等精密工具。The present invention relates to a stainless steel steel plate with high hardness and good surface quality, which is suitable for cutting tools such as kitchen knives or scissors, medical scalpels, knives such as knives or forks, spoons, and tweezers. tool.
菜刀或剪刀、醫療用手術刀等切削用具、及鑷子等精密工具之素材有時使用不鏽鋼鋼板。 例如,於菜刀之情形時,藉由衝壓加工等將不鏽鋼鋼板裁切或鍛造加工成既定形狀。繼而,對加工成既定形狀之不鏽鋼鋼板實施淬火處理、或淬火處理及回火處理而使之硬質化。然後,對硬質化之不鏽鋼鋼板實施開刃研磨(藉由研磨將成為刀尖之部分進行薄化之處理)等,製成最終製品(菜刀)。Stainless steel plates are sometimes used as materials for cutting tools such as kitchen knives, scissors, medical scalpels, and precision tools such as tweezers. For example, in the case of a kitchen knife, a stainless steel plate is cut or forged into a predetermined shape by pressing or the like. Then, the stainless steel sheet processed into a predetermined shape is hardened by quenching, or quenching and tempering. Then, the hardened stainless steel steel plate is subjected to blade grinding (a process of thinning the part that becomes the tip of the knife by grinding), etc., to produce a final product (kitchen knife).
作為上述切削用具及精密工具等用途所使用之不鏽鋼,例如可例舉:13 mass%Cr-0.3 mass%C鋼(JIS G 4304及JIS G 4305所規定之SUS420J2)等。As the stainless steel used for the above-mentioned cutting tools and precision tools, for example, 13 mass%Cr-0.3 mass%C steel (SUS420J2 specified in JIS G 4304 and JIS G 4305) can be mentioned.
然而,於切削用具及精密工具中,亦要求極力抑制由刀尖之磨耗所造成之鋒利程度之降低或鏽之產生,減少打磨等維護頻率。 近年來,該要求尤其不斷增高,市場對確保充分之耐蝕性、並且鋒利程度較高、進而能夠長期抑制由刀尖之磨耗所造成之鋒利程度之降低的高硬度之高級切削用具之需求正不斷增高。However, in cutting tools and precision tools, it is also required to minimize the sharpness reduction or the generation of rust caused by the wear of the tool tip, and to reduce the frequency of maintenance such as grinding. In recent years, this requirement has been increasing, and the market is constantly demanding high-grade cutting tools with high hardness that ensure sufficient corrosion resistance and have a high sharpness, which can inhibit the reduction of sharpness caused by the wear of the tool tip for a long time. Increase.
作為此種高硬度之高級切削用具所使用之不鏽鋼,例如可例舉:依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼。該依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼係與13 mass%Cr-0.3 mass%C鋼相比增加了C量而使硬度得以提高之鋼。 又,於專利文獻1中,揭示有 「一種不鏽鋼鋼帶,其特徵在於,包含:C:0.88 mass%以上且1.2 mass%以下、Cr:12.5 mass%以上且16.50 mass%以下、Si:0.05 mass%以上且0.20 mass%以下、N:0.001 mass%以上且0.02 mass%以下、Mn:1.0 mass%以下、Cu:1.0 mass%以下、P:0.03 mass%以下、S:0.010 mass%以下、及Ni:1.0 mass%以下,且剩餘部分包含Fe及不可避免之雜質。」。 [先前技術文獻] [專利文獻]As the stainless steel used for such high-hardness advanced cutting tools, for example, one can cite: 14 mass%Cr-0.5 mass%C steel according to the European unified standard: EN1.4116. This is based on the European unified standard: EN1.4116 14 mass%Cr-0.5 mass%C steel is a steel with increased C content compared with 13 mass%Cr-0.3 mass%C steel to increase the hardness. Also, in Patent Document 1, it is disclosed that "A stainless steel strip characterized by comprising: C: 0.88 mass% or more and 1.2 mass% or less, Cr: 12.5 mass% or more and 16.50 mass% or less, Si: 0.05 mass% or more and 0.20 mass% or less, N: 0.001 mass% or more and 0.02 mass% or less, Mn: 1.0 mass% or less, Cu: 1.0 mass% or less, P: 0.03 mass% or less, S: 0.010 mass% or less, and Ni: 1.0 mass% or less, and the remainder includes Fe and inevitable impurities.". [Prior Technical Literature] [Patent Literature]
[專利文獻1]日本專利第5010819號[Patent Document 1] Japanese Patent No. 5010819
(發明所欲解決之問題)(The problem to be solved by the invention)
然而,若對依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼或由專利文獻1所揭示之不鏽鋼鋼帶所獲得之鋼板實施研磨或開刃加工等,則存在以下情形:產生沿軋製方向之條紋圖案而大大損害外觀之美感。However, if the steel plate obtained according to the European unified standard: 14 mass%Cr-0.5 mass%C steel of EN1.4116 or the stainless steel strip disclosed in Patent Document 1 is ground or edged, there are the following situations : Produces a striped pattern along the rolling direction, which greatly impairs the aesthetics of the appearance.
於此種產生條紋圖案之情形時,需要進行追加研磨步驟等而去除條紋圖案。然而,研磨步驟之追加會導致製造成本之增加。又,於條紋圖案較為明顯之情形時,存在條紋圖案無法完全去除,或為了去除條紋圖案所需之研磨量變多從而無法獲得既定之形狀之情形。其結果,會導致良率及生產性之大幅度降低。In such a situation where the stripe pattern is generated, an additional polishing step or the like is required to remove the stripe pattern. However, the addition of the grinding step will increase the manufacturing cost. In addition, when the stripe pattern is obvious, the stripe pattern cannot be completely removed, or the amount of polishing required to remove the stripe pattern increases and the predetermined shape cannot be obtained. As a result, the yield and productivity are greatly reduced.
因此,現狀是要求開發一種於使用作為製品時具有較高硬度、且具有加工成製品時抑制條紋圖案產生之良好之表面品質的不鏽鋼鋼板。Therefore, the current situation requires the development of a stainless steel steel plate that has high hardness when used as a product and has a good surface quality that inhibits the occurrence of streak patterns when processed into a product.
本發明係鑒於上述現狀進行開發所得者,目的在於提供一種於使用作為製品時具有較高硬度(以下,亦簡稱為較高硬度)、且具有加工成製品時抑制條紋圖案產生之良好之表面品質(以下,亦簡稱為良好之表面品質)的不鏽鋼鋼板。 又,本發明之目的在於提供一種上述不鏽鋼鋼板之製造方法。 進而,本發明之目的在於提供一種使用上述不鏽鋼鋼板而成之切削用具及刀具。 再者,如上所述,本發明之不鏽鋼鋼板係將使用作為切削用具及刀具等製品時可獲得較高硬度者作為對象。即,本發明之不鏽鋼鋼板不僅包含硬質化之後(淬火處理後)之鋼板,亦包含硬質化之前(淬火處理前)之作為製品素材之鋼板。 (解決問題之技術手段)The present invention is developed in view of the above-mentioned current situation, and aims to provide a surface quality that has high hardness when used as a product (hereinafter also referred to as high hardness), and has a good surface quality that inhibits the occurrence of streak patterns when processed into a product. (Hereinafter, also referred to as "good surface quality") stainless steel steel plate. Furthermore, the object of the present invention is to provide a method for manufacturing the above-mentioned stainless steel plate. Furthermore, an object of the present invention is to provide a cutting tool and a tool using the above-mentioned stainless steel plate. Furthermore, as described above, the stainless steel sheet of the present invention targets those that can obtain higher hardness when used as products such as cutting tools and knives. That is, the stainless steel sheet of the present invention includes not only the steel sheet after hardening (after the quenching treatment), but also the steel sheet as the product material before the hardening (before the quenching treatment). (Technical means to solve the problem)
並且,本發明人等為了達成上述目的,反覆銳意研究。 首先,本發明人等對於在對依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼實施研磨或開刃加工(以下,亦簡稱為研磨)等之情形時產生條紋圖案之原因進行了研究。具體而言,藉由習知公知之方法於相同之條件下分別製造 ・具有依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼之成分組成之鋼板(以下,亦簡稱為鋼板a)、及 ・具有與由JIS G 4304及JIS G 4305所規定之SUS420J2相當之13 mass%Cr-0.3 mass%C鋼之成分組成的鋼板(以下,亦簡稱為鋼板b), 於相同之條件下對所製造之鋼板實施了研磨。 其結果,於鋼板b中,即便實施了研磨,亦未產生條紋圖案。另一方面,於鋼板a中,當實施研磨時,產生了條紋圖案。In addition, the inventors of the present invention have repeatedly studied in order to achieve the above-mentioned object. First of all, the inventors of the present invention are concerned about the occurrence of streak patterns when grinding or cutting (hereinafter, also referred to as grinding) steel 14 mass%Cr-0.5 mass%C according to the European unified standard: EN1.4116 The reasons were studied. Specifically, they are manufactured separately under the same conditions by conventional and well-known methods ・A steel plate with the composition of 14 mass%Cr-0.5 mass%C steel in accordance with the European unified standard: EN1.4116 (hereinafter also referred to as steel plate a), and ・A steel plate with a composition of 13 mass%Cr-0.3 mass%C steel equivalent to SUS420J2 specified by JIS G 4304 and JIS G 4305 (hereinafter also referred to as steel plate b), The steel plate manufactured was polished under the same conditions. As a result, in the steel plate b, even if polishing was performed, no streak pattern was generated. On the other hand, in the steel plate a, when polishing was performed, a striped pattern was generated.
根據上述結果,本發明人等考慮如下。 即,於鋼板a與鋼板b中,因成分組成之不同,即便於相同之製造條件下進行製造,析出物之析出狀態亦大不相同。並且,由於該析出物之析出狀態不同,故而於鋼板a中產生條紋圖案。Based on the above results, the inventors of the present invention considered the following. That is, in the steel sheet a and the steel sheet b, due to the difference in the component composition, even if it is manufactured under the same manufacturing conditions, the precipitation state of the precipitates is greatly different. In addition, since the precipitation state of the precipitates is different, a striped pattern is generated in the steel sheet a.
基於該考慮,本發明人等觀察鋼板a及鋼板b之金屬組織,將兩者詳細地進行對比。 其結果發現,如圖2所示,於產生了條紋圖案之鋼板a中,粗大之Cr系碳化物於金屬組織中於軋製方向上相連存在,成為產生條紋圖案之原因。 即,Cr系碳化物較不鏽鋼鋼板之母材(淬火前後皆是)更為硬質。因此,若金屬組織中存在粗大之Cr系碳化物,則於該Cr系碳化物存在之部位中,與其他部位相比,研磨量變少。其結果,於研磨後,局部產生凸部,其等以條紋圖案之形式顯現。 尤其是,於鋼板a(依據歐洲統一標準:EN1.4116之14 mass%Cr-0.5 mass%C鋼)之成分組成中,為了獲得更高之硬度,含有比鋼板b(13 mass%Cr-0.3 mass%C鋼)更多量之C或Cr。因此,於鋼板b中,即便藉由習知公知之方法進行製造,亦不會大量生成粗大之Cr系碳化物,但於以相同之條件所製造之鋼板a中,會大量生成粗大之Cr系碳化物,從而產生條紋圖案。Based on this consideration, the inventors of the present invention observed the metal structure of the steel plate a and the steel plate b, and compared the two in detail. As a result, it was found that, as shown in FIG. 2, in the steel sheet a with the striped pattern, the coarse Cr-based carbides are connected in the metal structure in the rolling direction, which is the cause of the striped pattern. That is, the Cr-based carbide is harder than the base material of the stainless steel steel plate (both before and after quenching). Therefore, if there are coarse Cr-based carbides in the metal structure, the amount of grinding is reduced in the locations where the Cr-based carbides exist, compared with other locations. As a result, after polishing, protrusions are locally generated, and they appear in the form of a striped pattern. In particular, in the composition of steel plate a (according to the European unified standard: 14 mass%Cr-0.5 mass%C steel in EN1.4116), in order to obtain higher hardness, it contains more than steel plate b(13 mass%Cr-0.3 mass%C steel) more C or Cr. Therefore, in the steel plate b, even if it is manufactured by a conventionally known method, a large amount of coarse Cr-based carbides will not be generated, but in the steel plate a manufactured under the same conditions, a large amount of coarse Cr-based carbides will be generated. Carbide, resulting in a striped pattern.
並且,本發明人等基於上述見解,進而反覆研究,獲得以下見解。 即,粒徑為2.0 μm以上之Cr系碳化物對研磨時條紋圖案之產生具有深刻影響。並且,藉由極力抑制此種粗大之Cr系碳化物之生成,尤其是,將粒徑為2.0 μm以上之Cr系碳化物之體積率抑制在10%以下,可大幅度抑制研磨時條紋圖案產生。In addition, the inventors of the present invention conducted repeated studies based on the above findings, and obtained the following findings. That is, Cr-based carbides with a particle size of 2.0 μm or more have a profound effect on the generation of streak patterns during polishing. In addition, by suppressing the formation of such coarse Cr carbides, especially by suppressing the volume ratio of Cr carbides with a particle size of 2.0 μm or more to 10% or less, the generation of streak patterns during polishing can be greatly suppressed. .
又,本發明人等進而反覆研究,獲得以下見解。 即,上述粗大之Cr系碳化物係鑄造時於鋼坯剖面之柱狀晶與等軸晶之交界附近沿鑄造方向所生成者。又,鑄造時所生成之粗大之Cr系碳氮化物於習知公知之一般製造條件下,在經過鑄造步驟之後之熱軋、熱軋板退火、冷軋及冷軋板退火步驟之後,依然殘留於軋製方向(與鑄造方向為相同方向)上。In addition, the inventors of the present invention conducted repeated studies and obtained the following findings. That is, the above-mentioned coarse Cr-based carbide system is formed in the casting direction near the boundary between the columnar crystals and the equiaxed crystals in the cross section of the billet during casting. In addition, the coarse Cr-based carbonitrides produced during casting still remain after the hot rolling, hot-rolled sheet annealing, cold-rolling, and cold-rolled sheet annealing steps after the casting step under conventional and well-known general manufacturing conditions. In the rolling direction (the same direction as the casting direction).
因此,本發明人等基於上述見解,對於獲得較高之硬度且防止粗大之Cr系碳化物生成之方法反覆研究。 其結果,獲得以下見解。 (1)適當地調整成分組成,尤其是,將C含量及Cr含量分別調整至0.45~0.60質量%、及13.0%以上且未滿16.0%之範圍, (2)此外,適當地控制鋼坯之加熱、熱軋及熱軋板退火條件, 具體而言,較為重要的是, (a)將鋼坯於1200~1350℃下保持30分鐘以上,且 (b)於熱軋中之軋製道次之中,將結束溫度為1050℃以上且軋縮率為20%以上之軋製道次數量設為3個道次以上, (c)又,將熱軋鋼板之捲取溫度設為600℃以上。 藉此,即便於含有一定量以上之C含量及Cr含量之情形時,亦可抑制粗大之Cr系碳化物生成,有效地防止研磨時條紋圖案產生。Therefore, the inventors of the present invention have repeatedly studied methods for obtaining higher hardness and preventing the formation of coarse Cr-based carbides based on the above findings. As a result, the following findings were obtained. (1) Appropriately adjust the component composition, in particular, adjust the C content and Cr content to 0.45 to 0.60 mass%, and 13.0% or more and less than 16.0% of the range, (2) In addition, appropriately control the heating, hot-rolling and annealing conditions of the hot-rolled steel billet, Specifically, more importantly, (a) Keep the billet at 1200~1350℃ for more than 30 minutes, and (b) Among the rolling passes in hot rolling, the number of rolling passes with a finishing temperature of 1050°C or higher and a reduction ratio of 20% or higher shall be 3 passes or more, (c) In addition, the coiling temperature of the hot-rolled steel sheet is set to 600°C or higher. Thereby, even when the C content and the Cr content are contained in a certain amount or more, the generation of coarse Cr-based carbides can be suppressed, and the generation of streak patterns during polishing can be effectively prevented.
再者,本發明人等對於藉由如上所述對製造條件進行控制而抑制粗大之Cr系碳化物生成之原因考慮如下。 即,如上述(2)(a)所示,藉由將鋼坯於1200~1350℃下保持30分鐘以上,可促進鑄造步驟中所生成之粗大之Cr系碳化物固溶於沃斯田鐵相(Cr系碳化物分解成Cr原子、C原子等,以原子狀態溶入至沃斯田鐵相中)。 又,於該狀態下,如上述(2)(b)所示,藉由於較高之溫度且較高之軋縮率下進行熱軋中之軋製道次,可進一步促進Cr系碳化物固溶於沃斯田鐵相。此外,軋製應變可被有效地賦予至鋼坯之板厚中央部。藉此,可消除於鋼坯之柱狀晶與等軸晶之交界部附近沿鑄造方向所生成之粗大之Cr系碳化物。又,可促進元素於位錯上之擴散(經由屬於晶格缺陷之位錯所引起之原子移動)。藉此,可更加促進Cr系碳化物固溶於沃斯田鐵相。進而,藉由促進沃斯田鐵相之動態再結晶及/或靜態再結晶,而使沃斯田鐵相之晶粒微細化。藉此,於上述(2)(c)中之熱軋鋼板之捲取時,自沃斯田鐵相之晶界析出之Cr系碳化物之析出位置增加,從而再析出之Cr系碳化物亦微細化。再者,所謂再結晶係自具有應變之晶粒內或晶界生成幾乎不包含應變之晶粒之現象。 藉由上述協同效應,即便於含有一定量之C含量及Cr含量之情形時,亦可抑制粗大之Cr系碳化物生成,防止研磨時條紋圖案產生。 本發明係基於上述見解,進一步加以研究而完成者。In addition, the inventors of the present invention considered the reasons for suppressing the formation of coarse Cr-based carbides by controlling the manufacturing conditions as described above. That is, as shown in (2)(a) above, by holding the billet at 1200 to 1350°C for more than 30 minutes, the coarse Cr-based carbides formed in the casting step can be promoted to dissolve in the austenitic iron phase. (Cr-based carbides are decomposed into Cr atoms, C atoms, etc., and dissolved in the austenitic iron phase in an atomic state). Also, in this state, as shown in (2)(b) above, the rolling pass in hot rolling at a higher temperature and a higher reduction ratio can further promote the solidification of Cr-based carbides. Dissolved in austenitic iron phase. In addition, rolling strain can be effectively imparted to the central part of the thickness of the billet. Thereby, the coarse Cr-based carbides generated along the casting direction near the boundary between the columnar crystals and the equiaxed crystals of the billet can be eliminated. In addition, it can promote the diffusion of elements on dislocations (atom movement caused by dislocations belonging to lattice defects). This can further promote the solid dissolution of the Cr-based carbides in the austenitic iron phase. Furthermore, by promoting the dynamic recrystallization and/or static recrystallization of the austenitic iron phase, the crystal grains of the austenitic iron phase are refined. As a result, during the coiling of the hot-rolled steel sheet in (2)(c) above, the precipitation position of the Cr-based carbides precipitated from the grain boundaries of the austenitic iron phase increases, so that the re-precipitated Cr-based carbides are also Micronization. Furthermore, the so-called recrystallization is a phenomenon in which crystal grains that hardly contain strain are generated from within grains or grain boundaries that have strain. With the above-mentioned synergistic effect, even when a certain amount of C content and Cr content is contained, the generation of coarse Cr carbides can be suppressed, and the generation of streak patterns during polishing can be prevented. The present invention was completed by further research based on the above-mentioned knowledge.
即,本發明之要點構成係如下所示。 1.一種不鏽鋼鋼板,其具有以下成分組成,該成分組成係以質量%計,含有: C:0.45~0.60%、 Si:0.05~1.00%、 Mn:0.05~1.00%、 P:0.05%以下、 S:0.020%以下、 Cr:13.0%以上且未滿16.0%、 Ni:0.10~1.00%及 N:0.010~0.200%, 剩餘部分包含Fe及不可避免之雜質;且 粒徑為2.0 μm以上之Cr系碳化物之合計體積率為10%以下。That is, the main point structure of the present invention is as follows. 1. A stainless steel steel plate having the following composition, which is calculated by mass% and contains: C: 0.45~0.60%, Si: 0.05~1.00%, Mn: 0.05~1.00%, P: 0.05% or less, S: 0.020% or less, Cr: 13.0% or more and less than 16.0%, Ni: 0.10~1.00% and N: 0.010~0.200%, The remainder contains Fe and unavoidable impurities; and The total volume ratio of Cr-based carbides with a particle size of 2.0 μm or more is 10% or less.
2.如上述1記載之不鏽鋼鋼板,其中,上述成分組成係以質量%計,進而含有自 Mo:0.05~1.00%、 Cu:0.05~1.00%及 Co:0.05~0.50% 之中選擇之1種或2種以上。2. The stainless steel sheet as described in 1 above, wherein the above-mentioned component composition is calculated by mass%, and further contains Mo: 0.05~1.00%, Cu: 0.05~1.00% and Co: 0.05~0.50% Choose one or more of them.
3.如上述1或2記載之不鏽鋼鋼板,其中,上述成分組成係以質量%計,進而含有自 Al:0.001~0.100%、 Ti:0.01~0.10%、 Nb:0.01~0.10%、 V:0.05~0.50%、 Zr:0.01~0.10%、 Mg:0.0002~0.0050%、 B:0.0002~0.0050%、 Ca:0.0003~0.0030%及 REM:0.01~0.10% 之中選擇之1種或2種以上。3. The stainless steel sheet as described in 1 or 2 above, wherein the above-mentioned component composition is calculated by mass%, and further contains Al: 0.001~0.100%, Ti: 0.01~0.10%, Nb: 0.01~0.10%, V: 0.05~0.50%, Zr: 0.01~0.10%, Mg: 0.0002~0.0050%, B: 0.0002~0.0050%, Ca: 0.0003~0.0030% and REM: 0.01~0.10% Choose one or more of them.
4.一種不鏽鋼鋼板之製造方法,其係用於製造上述1至3中任一項記載之不鏽鋼鋼板之方法;其包含有: 第1步驟,其將具有上述1至3中任一項記載之成分組成之鋼坯於1200~1350℃下保持30分鐘以上; 第2步驟,其對上述鋼坯實施熱軋而製成熱軋鋼板,並捲取該熱軋鋼板;及 第3步驟,其對上述熱軋鋼板實施熱軋板退火,並製成熱軋退火鋼板;且 上述第2步驟之熱軋中之軋製道次之中,結束溫度為1050℃以上且軋縮率為20%以上之軋製道次數量為3個道次以上,又,上述熱軋鋼板之捲取溫度為600℃以上, 上述第3步驟之熱軋板退火中之保持溫度為750~900℃,保持時間為10分鐘以上。4. A method for manufacturing a stainless steel plate, which is a method for manufacturing the stainless steel plate described in any one of 1 to 3 above; which includes: The first step is to hold a steel billet having the composition described in any one of 1 to 3 above at 1200 to 1350°C for more than 30 minutes; In the second step, hot-rolling the above-mentioned steel billet is made into a hot-rolled steel sheet, and the hot-rolled steel sheet is coiled; and The third step is to perform hot-rolled sheet annealing on the above-mentioned hot-rolled steel sheet and prepare a hot-rolled annealed steel sheet; and Among the rolling passes in the hot rolling of the second step, the number of rolling passes with an end temperature of 1050°C or higher and a reduction ratio of 20% or higher is 3 passes or more. The coiling temperature is above 600℃, The holding temperature in the hot-rolled sheet annealing in the third step is 750-900°C, and the holding time is 10 minutes or more.
5.如上述4記載之不鏽鋼鋼板之製造方法,其包含有第4步驟,該第4步驟係對上述熱軋退火鋼板實施冷軋而製成冷軋鋼板。5. The method for manufacturing a stainless steel sheet as described in 4 above, which includes a fourth step of performing cold rolling on the hot-rolled and annealed steel sheet to produce a cold-rolled steel sheet.
6.如上述5記載之不鏽鋼鋼板之製造方法,其包含有第5步驟,該第5步驟係對上述冷軋鋼板實施冷軋板退火而製成冷軋退火鋼板,且 上述冷軋板退火中之保持溫度為700~850℃,保持時間為5秒以上。6. The method for manufacturing a stainless steel sheet as described in 5 above, which includes a fifth step of performing cold-rolled sheet annealing on the cold-rolled steel sheet to prepare a cold-rolled annealed steel sheet, and The holding temperature during the annealing of the cold-rolled sheet is 700 to 850°C, and the holding time is 5 seconds or more.
7.如上述4至6中任一項記載之不鏽鋼鋼板之製造方法,其包含第6步驟,該第6步驟係對上述熱軋退火鋼板、上述冷軋鋼板或上述冷軋退火鋼板實施淬火處理,且 上述淬火處理中之保持溫度為950~1200℃,保持時間為5秒~30分鐘,保持後之平均冷卻速度為1℃/秒以上。7. The method for manufacturing a stainless steel sheet according to any one of 4 to 6 above, comprising a sixth step of subjecting the hot-rolled annealed steel sheet, the cold-rolled steel sheet or the cold-rolled annealed steel sheet to a quenching treatment ,and The holding temperature in the quenching treatment is 950 to 1200°C, the holding time is 5 seconds to 30 minutes, and the average cooling rate after holding is 1°C/sec or more.
8.如上述7記載之不鏽鋼鋼板之製造方法,其包含第7步驟,該第7步驟係對上述實施了淬火處理之鋼板實施回火處理,且 上述回火處理中之保持溫度為100~800℃,保持時間為5分鐘以上。8. The method for manufacturing a stainless steel sheet as described in 7 above, which includes a seventh step of performing tempering treatment on the above-mentioned quenched steel sheet, and The holding temperature in the above-mentioned tempering treatment is 100-800°C, and the holding time is more than 5 minutes.
9.一種切削用具,其係使用上述1至3中任一項記載之不鏽鋼鋼板而成。9. A cutting tool which is formed by using the stainless steel plate described in any one of 1 to 3 above.
10.一種刀具,其係使用上述1至3中任一項記載之不鏽鋼鋼板而成。 (對照先前技術之功效)10. A knife using the stainless steel plate described in any one of 1 to 3 above. (Compared with the effect of previous technology)
根據本發明,可獲得一種具有較高之硬度且具有良好之表面品質之不鏽鋼鋼板。According to the present invention, a stainless steel steel plate with high hardness and good surface quality can be obtained.
基於以下之實施形態對本發明進行說明。 首先,對於本發明之一實施形態之不鏽鋼鋼板之成分組成進行說明。再者,成分組成中之單位均為「質量%」,以下,只要沒有特別說明,僅以「%」表示。The present invention will be described based on the following embodiments. First, the composition of the stainless steel sheet in one embodiment of the present invention will be described. In addition, the unit in the composition of the ingredients is all "mass%". Below, unless otherwise specified, it is only expressed as "%".
C:0.45~0.60% C係具有使藉由淬火處理所獲得之麻田散鐵相硬質化之效果。此處,若C含量未滿0.45%,則淬火處理後之硬度不足,無法充分獲得高級切削用具所要求之鋒利程度。另一方面,若C含量超過0.60%,則即便適當地控制製造條件,亦無法充分地抑制粗大之碳化物之產生,無法獲得良好之表面品質。又,於淬火處理時容易產生淬火裂紋,從而難以穩定地製造切削用具。 因此,C含量設為0.45~0.60%之範圍。C含量較佳為0.55%以下,更佳為0.50%以下。C: 0.45~0.60% The C series has the effect of hardening the Asada scattered iron phase obtained by quenching. Here, if the C content is less than 0.45%, the hardness after quenching is insufficient, and the sharpness required for high-end cutting tools cannot be sufficiently obtained. On the other hand, if the C content exceeds 0.60%, even if the manufacturing conditions are appropriately controlled, the generation of coarse carbides cannot be sufficiently suppressed, and good surface quality cannot be obtained. In addition, quenching cracks are likely to occur during the quenching treatment, and it is difficult to stably manufacture the cutting tool. Therefore, the C content is set to the range of 0.45 to 0.60%. The C content is preferably 0.55% or less, more preferably 0.50% or less.
Si:0.05~1.00% Si係於熔製鋼時作為去氧劑而發揮作用。為了獲得此種效果,Si含量設為0.05%以上。然而,若Si含量超過1.00%,則鋼板於淬火處理前過度硬質化,無法充分地獲得成形為切削用具等既定形狀時之加工性。 因此,Si含量設為0.05~1.00%之範圍。Si含量較佳為0.20%以上。又,Si含量較佳為0.60%以下。Si: 0.05~1.00% The Si system functions as an oxygen scavenger when steel is melted. In order to obtain such an effect, the Si content is set to 0.05% or more. However, if the Si content exceeds 1.00%, the steel sheet becomes excessively hardened before the quenching treatment, and it is impossible to sufficiently obtain workability when formed into a predetermined shape such as a cutting tool. Therefore, the Si content is set to the range of 0.05 to 1.00%. The Si content is preferably 0.20% or more. Furthermore, the Si content is preferably 0.60% or less.
Mn:0.05~1.00% Mn係具有促進沃斯田鐵相之生成且提高淬火性之效果。為了獲得此種效果,Mn含量設為0.05%以上。然而,若Mn含量超過1.00%,則導致耐蝕性降低。 因此,Mn含量設為0.05~1.00%之範圍。Mn含量較佳為0.40%以上。又,Mn含量較佳為0.80%以下。Mn: 0.05~1.00% The Mn series has the effect of promoting the formation of austenitic iron phase and improving the hardenability. In order to obtain such an effect, the Mn content is set to 0.05% or more. However, if the Mn content exceeds 1.00%, the corrosion resistance will decrease. Therefore, the Mn content is set to the range of 0.05 to 1.00%. The Mn content is preferably 0.40% or more. In addition, the Mn content is preferably 0.80% or less.
P:0.05%以下 P係助長由晶界偏析所造成之晶界破壞之元素。因此,較理想為儘可能減少P。 因此,P含量設為0.05%以下。P含量較佳為0.04%以下,更佳為0.03%以下。 再者,P含量之下限並無特別限定。但,過度脫P會導致成本增加,因此P含量較佳為0.005%以上。P: Below 0.05% P is an element that promotes the destruction of grain boundaries caused by grain boundary segregation. Therefore, it is desirable to reduce P as much as possible. Therefore, the P content is set to 0.05% or less. The P content is preferably 0.04% or less, more preferably 0.03% or less. In addition, the lower limit of the P content is not particularly limited. However, excessive P removal will increase the cost, so the P content is preferably 0.005% or more.
S:0.020%以下 S係以MnS等硫化物系中介物之形式存在於鋼中而使延展性或耐蝕性等降低之元素。因此,較理想為儘可能減少S。 因此,S含量設為0.020%以下。S含量較佳為0.015%以下。 再者,S含量之下限並無特別限定。但,過度脫S會導致成本增加,因此S含量較佳為0.0005%以上。S: Below 0.020% S is an element that exists in steel in the form of a sulfide-based intermediary such as MnS and reduces ductility or corrosion resistance. Therefore, it is desirable to reduce S as much as possible. Therefore, the S content is set to 0.020% or less. The S content is preferably 0.015% or less. In addition, the lower limit of the S content is not particularly limited. However, excessive S removal will increase the cost, so the S content is preferably 0.0005% or more.
Cr:13.0%以上且未滿16.0% Cr係具有提高耐蝕性之效果。為了獲得此種效果,Cr含量設為13.0%以上。然而,若Cr含量變為16.0%以上,則淬火處理之加熱、保持時所生成之沃斯田鐵量減少。因此,淬火處理後所獲得之麻田散鐵相減少,無法獲得充分之硬度。因此,Cr含量設為13.0%以上且未滿16.0%之範圍。Cr含量較佳為14.0%以上。又,Cr含量較佳為15.5%以下,更佳為15.0%以下。Cr: 13.0% or more and less than 16.0% Cr series has the effect of improving corrosion resistance. In order to obtain such an effect, the Cr content is set to 13.0% or more. However, if the Cr content becomes 16.0% or more, the amount of austenitic iron produced during the heating and holding of the quenching treatment decreases. Therefore, the Asada scattered iron phase obtained after the quenching treatment is reduced, and sufficient hardness cannot be obtained. Therefore, the Cr content is set to a range of 13.0% or more and less than 16.0%. The Cr content is preferably 14.0% or more. Furthermore, the Cr content is preferably 15.5% or less, more preferably 15.0% or less.
Ni:0.10~1.00% Ni係具有提高耐蝕性且提高淬火後之韌性之效果。為了獲得此種效果,Ni含量設為0.10%以上。然而,若Ni含量超過1.00%,則該效果飽和。又,固溶Ni量之增加會使得鋼板於淬火處理前過度硬質化,無法充分地獲得成形為切削用具等既定形狀時之加工性。 因此,Ni含量設為0.10~1.00%之範圍。Ni含量較佳為0.15%以上,更佳為0.20%以上。又,Ni含量較佳為0.80%以下,更佳為0.60%以下。Ni: 0.10~1.00% Ni series has the effect of improving corrosion resistance and improving toughness after quenching. In order to obtain such an effect, the Ni content is set to 0.10% or more. However, if the Ni content exceeds 1.00%, the effect is saturated. In addition, the increase in the amount of solute Ni makes the steel sheet excessively hardened before the quenching treatment, and the workability when formed into a predetermined shape such as a cutting tool cannot be sufficiently obtained. Therefore, the Ni content is set to the range of 0.10% to 1.00%. The Ni content is preferably 0.15% or more, more preferably 0.20% or more. In addition, the Ni content is preferably 0.80% or less, more preferably 0.60% or less.
N:0.010~0.200% N與C同樣地,係具有使藉由淬火處理所獲得之麻田散鐵相硬質化之效果。又,N亦具有提高淬火處理後之耐蝕性之效果。為了獲得此種效果,N含量設為0.010%以上。然而,若N含量超過0.200%,則鑄造時會產生氣泡,從而引發表面缺陷之產生。 因此,N含量設為0.010~0.200%之範圍。N含量較佳為0.015%以上,更佳為0.020%以上。又,N含量較佳為0.150%以下,更佳為0.100%以下。N: 0.010~0.200% N, like C, has the effect of hardening the Asada scattered iron phase obtained by quenching. In addition, N also has the effect of improving the corrosion resistance after quenching. In order to obtain such an effect, the N content is set to 0.010% or more. However, if the N content exceeds 0.200%, bubbles will be generated during casting, which will cause surface defects. Therefore, the N content is set to the range of 0.010% to 0.200%. The N content is preferably 0.015% or more, more preferably 0.020% or more. Furthermore, the N content is preferably 0.150% or less, more preferably 0.100% or less.
以上,對本發明之一實施形態之不鏽鋼鋼板之基本成分組成進行了說明,但可進而含有 自Mo:0.05~1.00%、Cu:0.05~1.00%及Co:0.05~0.50%之中選擇之1種或2種以上、 及/或 自Al:0.001~0.100%、Ti:0.01~0.10%、Nb:0.01~0.10%、V:0.05~0.50%、Zr:0.01~0.10%、Mg:0.0002~0.0050%、B:0.0002~0.0050%、Ca:0.0003~0.0030%及REM:0.01~0.10%之中選擇之1種或2種以上。Above, the basic composition of the stainless steel sheet of one embodiment of the present invention has been described, but it may further contain Choose one or more types from Mo: 0.05 to 1.00%, Cu: 0.05 to 1.00%, and Co: 0.05 to 0.50%, And/or From Al: 0.001 to 0.100%, Ti: 0.01 to 0.10%, Nb: 0.01 to 0.10%, V: 0.05 to 0.50%, Zr: 0.01 to 0.10%, Mg: 0.0002 to 0.0050%, B: 0.0002 to 0.0050%, One or more of Ca: 0.0003 to 0.0030% and REM: 0.01 to 0.10%.
Mo:0.05~1.00% Mo係具有提高耐蝕性之效果。為了獲得此種效果,Mo含量較佳為0.05%以上。然而,若Mo含量超過1.00%,則淬火處理之加熱、保持時所生成之沃斯田鐵量減少,於淬火處理後無法獲得充分之硬度。 因此,於含有Mo之情形時,Mo含量較佳係設為0.05~1.00%之範圍。Mo含量更佳為0.10%以上,進而較佳為0.50%以上。又,Mo含量更佳為0.80%以下,進而較佳為0.65%以下。Mo: 0.05~1.00% Mo series have the effect of improving corrosion resistance. In order to obtain such an effect, the Mo content is preferably 0.05% or more. However, if the Mo content exceeds 1.00%, the amount of austenitic iron generated during the heating and holding of the quenching treatment decreases, and sufficient hardness cannot be obtained after the quenching treatment. Therefore, when Mo is contained, the Mo content is preferably set to be in the range of 0.05 to 1.00%. The Mo content is more preferably 0.10% or more, and still more preferably 0.50% or more. In addition, the Mo content is more preferably 0.80% or less, and still more preferably 0.65% or less.
Cu:0.05~1.00% Cu係具有於淬火處理後之鋼板中提高回火軟化阻力之效果。為了獲得此種效果,Cu含量較佳係設為0.05%以上。然而,若Cu含量超過1.00%,則導致耐蝕性降低。 因此,於含有Cu之情形時,Cu含量較佳係設為0.05~1.00%之範圍。Cu含量更佳為0.10%以上。又,Cu含量更佳為0.50%以下,進而較佳為0.20%以下。Cu: 0.05~1.00% Cu has the effect of increasing the temper softening resistance in the steel plate after the quenching treatment. In order to obtain such an effect, the Cu content is preferably set to 0.05% or more. However, if the Cu content exceeds 1.00%, the corrosion resistance will decrease. Therefore, when Cu is contained, the Cu content is preferably set to the range of 0.05% to 1.00%. The Cu content is more preferably 0.10% or more. In addition, the Cu content is more preferably 0.50% or less, and still more preferably 0.20% or less.
Co:0.05~0.50% Co係具有提高韌性之效果。為了獲得此種效果,Co含量較佳係設為0.05%以上。然而,若Co含量超過0.50%,則於淬火處理前,無法充分地獲得使鋼板成形為切削用具等既定形狀時之加工性。 因此,於含有Co之情形時,Co含量較佳係設為0.05~0.50%之範圍。Co含量更佳為0.10%以上。又,Co含量更佳為0.20%以下。Co: 0.05~0.50% Co series has the effect of improving toughness. In order to obtain such an effect, the Co content is preferably set to 0.05% or more. However, if the Co content exceeds 0.50%, the workability when forming the steel sheet into a predetermined shape such as a cutting tool cannot be sufficiently obtained before the quenching treatment. Therefore, when Co is contained, the Co content is preferably set to the range of 0.05% to 0.50%. The Co content is more preferably 0.10% or more. In addition, the Co content is more preferably 0.20% or less.
Al:0.001~0.100% Al與Si同樣地,係作為去氧劑而發揮作用。為了獲得此種效果,Al含量較佳係設為0.001%以上。然而,若Al含量超過0.100%,則淬火性降低。 因此,於含有Al之情形時,Al含量較佳係設為0.001~0.100%之範圍。Al含量更佳為0.050%以下,進而較佳為0.010%以下。Al: 0.001~0.100% Al, like Si, functions as an oxygen scavenger. In order to obtain such an effect, the Al content is preferably set to 0.001% or more. However, if the Al content exceeds 0.100%, the hardenability decreases. Therefore, when Al is contained, the Al content is preferably set to be in the range of 0.001 to 0.100%. The Al content is more preferably 0.050% or less, and still more preferably 0.010% or less.
Ti:0.01~0.10% Ti與Cr同樣地,係與C及N之親和力較高而於鋼中形成碳化物之元素。又,Ti係具有提高回火軟化阻力之效果。因此,於進行回火時可抑制軟質化,且提高韌性。為了獲得此種效果,Ti含量較佳係設為0.01%以上。然而,若Ti含量超過0.10%,則該效果飽和。又,反而韌性降低。 因此,於含有Ti之情形時,Ti含量較佳係設為0.01~0.10%之範圍。Ti含量更佳為0.02%以上。又,Ti含量更佳為0.05%以下。Ti: 0.01~0.10% Ti, like Cr, is an element that has a higher affinity for C and N and forms carbides in steel. In addition, the Ti system has the effect of increasing the tempering softening resistance. Therefore, when tempering is performed, softening can be suppressed and toughness can be improved. In order to obtain such an effect, the Ti content is preferably set to 0.01% or more. However, if the Ti content exceeds 0.10%, the effect is saturated. Moreover, on the contrary, the toughness decreases. Therefore, when Ti is contained, the Ti content is preferably set to a range of 0.01% to 0.10%. The Ti content is more preferably 0.02% or more. In addition, the Ti content is more preferably 0.05% or less.
Nb:0.01~0.10% Nb與Ti同樣地,係與C及N之親和力較高而於鋼中形成碳化物之元素。又,Nb係具有提高回火軟化阻力之效果。因此,於進行回火時可抑制軟質化,且提高韌性。為了獲得此種效果,Nb含量較佳係設為0.01%以上。然而,若Nb含量超過0.10%,則該效果飽和。又,存在因金屬間化合物之析出而導致韌性降低之情形。 因此,於含有Nb之情形時,Nb含量較佳係設為0.01~0.10%之範圍。Nb含量更佳為0.02%以上。又,Nb含量更佳為0.05%以下。Nb: 0.01~0.10% Nb, like Ti, is an element that has a higher affinity for C and N and forms carbides in steel. In addition, the Nb system has the effect of increasing the temper softening resistance. Therefore, when tempering is performed, softening can be suppressed and toughness can be improved. In order to obtain such an effect, the Nb content is preferably set to 0.01% or more. However, if the Nb content exceeds 0.10%, the effect is saturated. In addition, there are cases where the toughness decreases due to the precipitation of intermetallic compounds. Therefore, when Nb is contained, the Nb content is preferably set to the range of 0.01 to 0.10%. The Nb content is more preferably 0.02% or more. In addition, the Nb content is more preferably 0.05% or less.
V:0.05~0.50% V與Ti或Nb同樣地,係與C及N之親和力較高而於鋼中形成碳化物之元素。又,V係具有提高回火軟化阻力之效果。因此,於進行回火時可抑制軟質化,且提高韌性。為了獲得此種效果,V含量較佳係設為0.05%以上。然而,若V含量超過0.50%,則該效果飽和。又,存在因金屬間化合物之析出而導致韌性降低之情形。 因此,於含有V之情形時,V含量較佳係設為0.05~0.50%之範圍。V含量更佳為0.10%以上。又,V含量更佳為0.30%以下,進而較佳為0.20%以下。V: 0.05~0.50% V, like Ti or Nb, is an element that has a higher affinity for C and N and forms carbides in steel. In addition, the V series has the effect of increasing the tempering softening resistance. Therefore, when tempering is performed, softening can be suppressed and toughness can be improved. In order to obtain such an effect, the V content is preferably set to 0.05% or more. However, if the V content exceeds 0.50%, the effect is saturated. In addition, there are cases where the toughness decreases due to the precipitation of intermetallic compounds. Therefore, when V is contained, the V content is preferably set to the range of 0.05% to 0.50%. The V content is more preferably 0.10% or more. In addition, the V content is more preferably 0.30% or less, and still more preferably 0.20% or less.
Zr:0.01~0.10% Zr與Ti或Nb同樣地,係與C及N之親和力較高而於鋼中形成碳化物之元素。又,Zr係具有提高回火軟化阻力之效果。因此,於進行回火時可抑制軟質化,且提高韌性。為了獲得此種效果,Zr含量較佳係設為0.01%以上。然而,若Zr含量超過0.10%,則該效果飽和。又,存在因金屬間化合物之析出而導致韌性降低之情形。 因此,於含有Zr之情形時,Zr含量較佳係設為0.01~0.10%之範圍。Zr含量更佳為0.02%以上。又,Zr含量更佳為0.05%以下。Zr: 0.01~0.10% Zr, like Ti or Nb, is an element that has a higher affinity for C and N and forms carbides in steel. In addition, the Zr system has the effect of increasing the tempering softening resistance. Therefore, when tempering is performed, softening can be suppressed and toughness can be improved. In order to obtain such an effect, the Zr content is preferably set to 0.01% or more. However, if the Zr content exceeds 0.10%, the effect is saturated. In addition, there are cases where the toughness decreases due to the precipitation of intermetallic compounds. Therefore, when Zr is contained, the Zr content is preferably set to the range of 0.01 to 0.10%. The Zr content is more preferably 0.02% or more. In addition, the Zr content is more preferably 0.05% or less.
Mg:0.0002~0.0050% Mg係具有提高鋼坯之等軸晶率、提高加工性或韌性之效果。為了獲得此種效果,Mg含量較佳係設為0.0002%以上。然而,若Mg含量超過0.0050%,則存在鋼板之表面性狀變差之情形。 因此,於含有Mg之情形時,Mg含量較佳係設為0.0002~0.0050%之範圍。Mg含量更佳為0.0010%以上。又,Mg含量更佳為0.0020%以下。Mg: 0.0002~0.0050% Mg has the effect of increasing the equiaxed crystal ratio of the steel billet and improving the workability or toughness. In order to obtain such an effect, the Mg content is preferably set to 0.0002% or more. However, if the Mg content exceeds 0.0050%, the surface properties of the steel sheet may deteriorate. Therefore, when Mg is contained, the Mg content is preferably set to the range of 0.0002% to 0.0050%. The Mg content is more preferably 0.0010% or more. In addition, the Mg content is more preferably 0.0020% or less.
B:0.0002~0.0050% B係具有於鑄造及熱軋時提高熱加工性之效果。又,B係偏析於肥粒鐵相及沃斯田鐵相之晶界而使晶界強度提昇。藉此,抑制鑄造及熱軋時產生裂紋。為了獲得此種效果,B含量較佳係設為0.0002%以上。然而,若B含量超過0.0050%,則於淬火處理前,無法充分地獲得使鋼板成形為切削用具等既定形狀時之加工性。又,導致韌性降低。 因此,於含有B之情形時,B含量較佳係設為0.0002~0.0050%之範圍。B含量更佳為0.0005%以上。又,B含量更佳為0.0030%以下,進而較佳為0.0020%以下。B: 0.0002~0.0050% B series has the effect of improving hot workability during casting and hot rolling. In addition, the B series segregates in the grain boundaries of the fat iron phase and the austenitic iron phase to increase the strength of the grain boundaries. This suppresses the occurrence of cracks during casting and hot rolling. In order to obtain such an effect, the B content is preferably set to 0.0002% or more. However, if the B content exceeds 0.0050%, the workability at the time of forming the steel sheet into a predetermined shape such as a cutting tool cannot be sufficiently obtained before the quenching treatment. In addition, the toughness decreases. Therefore, when B is contained, the B content is preferably set to the range of 0.0002% to 0.0050%. The B content is more preferably 0.0005% or more. In addition, the B content is more preferably 0.0030% or less, and still more preferably 0.0020% or less.
Ca:0.0003~0.0030% Ca係具有使冶煉暨連續鑄造時所生成之中介物微細化之效果,尤其是對於防止連續鑄造中之噴嘴之堵塞較為有效。為了獲得此種效果,Ca含量較佳係設為0.0003%以上。然而,若Ca含量超過0.0030%,則存在因CaS之生成而使耐蝕性降低之情形。 因此,於含有Ca之情形時,Ca含量較佳係設為0.0003~0.0030%之範圍。Ca含量更佳為0.0005%以上,進而較佳為0.0007%以上。又,Ca含量更佳為0.0020%以下,進而較佳為0.0015%以下。Ca: 0.0003~0.0030% The Ca system has the effect of miniaturizing the intermediary produced during smelting and continuous casting, and is especially effective in preventing nozzle clogging in continuous casting. In order to obtain such an effect, the Ca content is preferably set to 0.0003% or more. However, if the Ca content exceeds 0.0030%, the corrosion resistance may decrease due to the formation of CaS. Therefore, when Ca is contained, the content of Ca is preferably set to the range of 0.0003% to 0.0030%. The Ca content is more preferably 0.0005% or more, and still more preferably 0.0007% or more. In addition, the Ca content is more preferably 0.0020% or less, and still more preferably 0.0015% or less.
REM:0.01~0.10% 稀土類金屬(REM,Rare Earth Metals)係具有提高熱延展性之效果。又,REM亦具有抑制熱軋時之鋼板端面部之裂紋或肌理粗糙之效果。為了獲得此種效果,REM含量較佳係設為0.01%以上。然而,若REM含量超過0.10%,則該效果飽和。又,REM亦為昂貴元素。 因此,於含有REM之情形時,REM含量較佳係設為0.01~0.10%之範圍。REM含量更佳為0.05%以下。REM: 0.01~0.10% Rare Earth Metals (REM, Rare Earth Metals) have the effect of improving thermal ductility. In addition, REM also has the effect of suppressing cracks or rough texture on the end face of the steel sheet during hot rolling. In order to obtain such an effect, the REM content is preferably set to 0.01% or more. However, if the REM content exceeds 0.10%, the effect is saturated. Moreover, REM is also an expensive element. Therefore, when REM is contained, the REM content is preferably set to a range of 0.01% to 0.10%. The REM content is more preferably 0.05% or less.
上述以外之成分之剩餘部分為Fe及不可避免之雜質。The remainder of the components other than the above is Fe and unavoidable impurities.
其次,對於本發明之一實施形態之不鏽鋼鋼板之金屬組織進行說明。 本發明之一實施形態之不鏽鋼鋼板之金屬組織於淬火處理之前後,成為主體之組織發生變化。 例如,於將本發明之一實施形態之不鏽鋼鋼板加工成製品之情形時,首先,於鋼板未硬質化之階段中,藉由衝壓加工等將鋼板裁切或鍛造加工成既定形狀。繼而,對加工成既定形狀之鋼板實施淬火處理、或淬火及回火處理而使之硬質化。亦即,於淬火處理之前後,使成為主體之組織發生變化,具體而言,使之自肥粒鐵相變化成麻田散鐵相。 但,粒徑為2.0 μm以上之Cr系碳化物即便於淬火處理之前後仍變化不大,且大致維持不變。 因此,於本發明之一實施形態之不鏽鋼鋼板之金屬組織中,不論淬火處理前後,極為重要的是將粒徑為2.0 μm以上之Cr系碳化物之體積率設為10%以下。Next, the metal structure of the stainless steel sheet in one embodiment of the present invention will be described. The metal structure of the stainless steel steel plate in one embodiment of the present invention changes in the main structure before and after the quenching treatment. For example, when processing the stainless steel sheet of one embodiment of the present invention into a product, first, in a stage where the steel sheet is not hardened, the steel sheet is cut or forged into a predetermined shape by press working or the like. Then, the steel plate processed into a predetermined shape is subjected to quenching treatment, or quenching and tempering treatment to harden it. That is, before and after the quenching treatment, the main structure is changed, specifically, from the fat grain iron phase to the Asada scattered iron phase. However, the Cr-based carbides with a particle size of 2.0 μm or more did not change much even before and after the quenching treatment, and remained almost unchanged. Therefore, in the metallic structure of the stainless steel sheet according to one embodiment of the present invention, it is extremely important to set the volume ratio of Cr-based carbides with a particle size of 2.0 μm or more to 10% or less, regardless of before and after quenching.
粒徑為2.0 μm以上之Cr系碳化物之體積率:10%以下 Cr系碳化物係較不鏽鋼鋼板之母材(淬火前後皆是)更為硬質。因此,若於在金屬組織中存在大量粗大之Cr系碳化物、尤其是粒徑為2.0 μm以上之Cr系碳化物之狀態下實施研磨或開刃加工等,則於該Cr系碳化物存在之部位中,與其他部位相比,研磨量變少。其結果,於研磨後,局部產生凸部,其等以條紋圖案之形式顯現。 因此,粒徑為2.0 μm以上之Cr系碳化物之體積率設為10%以下。粒徑為2.0 μm以上之Cr系碳化物之體積率較佳為5%以下,更佳為2%以下。再者,粒徑為2.0 μm以上之Cr系碳化物之體積率亦可為0%。 再者,關於粒徑未滿2.0 μm之Cr系碳化物,於研磨時,不會產生肉眼可識別之程度之凹凸,不參與條紋圖案之產生。因此,粒徑未滿2.0 μm之Cr系碳化物之體積率並無特別限定。Volume ratio of Cr-based carbides with a particle size of 2.0 μm or more: 10% or less Cr-based carbides are harder than the base material of stainless steel steel plates (both before and after quenching). Therefore, if a large amount of coarse Cr-based carbides are present in the metal structure, especially Cr-based carbides with a particle size of 2.0 μm or more, grinding or edge processing is performed, and the Cr-based carbides are present in the metal structure. Among the parts, the amount of polishing is reduced compared to other parts. As a result, after polishing, protrusions are locally generated, and they appear in the form of a striped pattern. Therefore, the volume ratio of Cr-based carbides with a particle size of 2.0 μm or more is set to 10% or less. The volume ratio of Cr-based carbides with a particle size of 2.0 μm or more is preferably 5% or less, more preferably 2% or less. Furthermore, the volume ratio of Cr-based carbides with a particle size of 2.0 μm or more can also be 0%. In addition, the Cr-based carbides with a particle size of less than 2.0 μm will not produce unevenness that can be recognized by the naked eye during grinding, and will not participate in the production of stripe patterns. Therefore, the volume ratio of Cr-based carbides with a particle size of less than 2.0 μm is not particularly limited.
又,此處所指之Cr系碳化物主要為Cr23 C6 。又,Cr碳化物中之一部分Cr被Fe或Mn、Ti、Nb、V、Zr等元素取代而成者、或一部分C被N取代而成者亦包含於此處所指之Cr系碳化物。In addition, the Cr-based carbide referred to here is mainly Cr 23 C 6 . In addition, the Cr carbides in which a part of Cr is replaced by elements such as Fe or Mn, Ti, Nb, V, Zr, or the parts in which C is replaced by N are also included in the Cr-based carbides referred to herein.
又,本發明之一實施形態之不鏽鋼鋼板中之Cr系碳化物以外之組織成為肥粒鐵相與麻田散鐵相之合計體積率為95%以上、更佳為98%以上之金屬組織。肥粒鐵相與麻田散鐵相之合計體積率亦可為100%。作為肥粒鐵相、麻田散鐵相及上述Cr系碳化物以外之剩餘部分組織,可例舉:殘留沃斯田鐵相或其他析出物(亦包含粒徑未滿2.0 μm之Cr系碳化物)、中介物(例如,Al或Si等之氧化物及Mn等之硫化物等)。剩餘部分組織之體積率較佳為5%以下,更佳為2%以下。剩餘部分組織之體積率亦可為0%。 再者,於本發明之一實施形態之不鏽鋼鋼板中包含淬火處理前後之兩種鋼板,例如包含:熱軋鋼板、熱軋退火鋼板、冷軋鋼板及冷軋退火鋼板暨對該等鋼板實施淬火處理及/或回火處理所獲得之鋼板(下述淬火處理鋼板及回火處理鋼板)等。In addition, the structure other than the Cr-based carbides in the stainless steel sheet of one embodiment of the present invention becomes a metallic structure with a total volume ratio of the ferrite phase and the Asada scattered iron phase of 95% or more, more preferably 98% or more. The total volume ratio of the fertilizer grain iron phase and the Asada scattered iron phase can also be 100%. Examples of the remaining part of the structure other than the ferrous iron phase, the Asada scattered iron phase, and the aforementioned Cr-based carbides include: residual austenitic iron phase or other precipitates (including Cr-based carbides with a particle size of less than 2.0 μm) ), intermediates (for example, oxides such as Al or Si, sulfides such as Mn, etc.). The volume ratio of the remaining part of the tissue is preferably 5% or less, more preferably 2% or less. The volume ratio of the remaining part of the tissue can also be 0%. Furthermore, the stainless steel sheet of one embodiment of the present invention includes two kinds of steel sheets before and after the quenching treatment, such as: hot-rolled steel sheets, hot-rolled annealed steel sheets, cold-rolled steel sheets, and cold-rolled annealed steel sheets, and quenching these steel sheets Steel plates obtained by treatment and/or tempering treatment (the following quenched steel plates and tempered steel plates), etc.
再者,於熱軋鋼板、熱軋退火鋼板、冷軋鋼板及冷軋退火鋼板之階段中,Cr系碳化物以外之組織係成為肥粒鐵相主體之組織。 具體而言,成為肥粒鐵相之體積率為80%以上、較佳為90%以上、更佳為95%以上、進而較佳為98%以上之金屬組織。肥粒鐵相之體積率亦可為100%。作為肥粒鐵相及上述Cr系碳化物以外之剩餘部分組織,可例舉:麻田散鐵相或殘留沃斯田鐵相、其他析出物(亦包含粒徑未滿2.0 μm之Cr系碳化物)、中介物(例如,Al或Si等之氧化物及Mn等之硫化物等)。剩餘部分組織之體積率較佳為20%以下,更佳為10%以下,進而較佳為5%以下,進而更佳為2%以下。剩餘部分組織之體積率亦可為0%。 再者,熱軋鋼板除了包含熱軋狀態之鋼板以外,亦包含對熱軋狀態之鋼板實施酸洗等去除氧化皮之處理所獲得之鋼板。又,熱軋退火鋼板除了包含對熱軋鋼板實施熱軋板退火所獲得之鋼板以外,亦包含對該實施熱軋板退火所獲得之鋼板進而實施酸洗等去除氧化皮之處理所獲得之鋼板。冷軋鋼板除了包含冷軋狀態之鋼板以外,亦包含對冷軋狀態之鋼板實施酸洗等去除氧化皮之處理所獲得之鋼板。Furthermore, in the stages of hot-rolled steel sheet, hot-rolled and annealed steel sheet, cold-rolled steel sheet, and cold-rolled and annealed steel sheet, the structure other than the Cr-based carbides becomes the main structure of the ferrous iron phase. Specifically, the volume ratio of the ferrous iron phase is 80% or more, preferably 90% or more, more preferably 95% or more, and still more preferably 98% or more of the metallic structure. The volume ratio of the ferrite phase can also be 100%. Examples of the rest of the structure other than the ferrous iron phase and the aforementioned Cr-based carbides include: Asada scattered iron phase or residual austenitic iron phase, and other precipitates (including Cr-based carbides with a particle size of less than 2.0 μm) ), intermediates (for example, oxides such as Al or Si, sulfides such as Mn, etc.). The volume ratio of the remaining part of the tissue is preferably 20% or less, more preferably 10% or less, still more preferably 5% or less, and still more preferably 2% or less. The volume ratio of the remaining part of the tissue can also be 0%. Furthermore, the hot-rolled steel sheet includes not only the steel sheet in the hot-rolled state, but also the steel sheet obtained by performing a treatment such as pickling to remove the oxide scale on the hot-rolled steel sheet. In addition, the hot-rolled annealed steel sheet includes not only the steel sheet obtained by performing hot-rolled sheet annealing on the hot-rolled steel sheet, but also the steel sheet obtained by subjecting the steel sheet obtained by performing the hot-rolled sheet annealing treatment to pickling and other descaling treatments. . In addition to cold-rolled steel sheets, cold-rolled steel sheets also include steel sheets obtained by pickling the cold-rolled steel sheets to remove oxide scales.
進而,於對熱軋鋼板、熱軋退火鋼板、冷軋鋼板及冷軋退火鋼板實施淬火處理所得之鋼板(以下,亦稱為淬火處理鋼板)中,Cr系碳化物以外之組織係成為麻田散鐵相主體之組織。 具體而言,成為麻田散鐵相之體積率為80%以上、較佳為90%以上、更佳為95%以上、進而較佳為98%以上之金屬組織。麻田散鐵相之體積率亦可為100%。作為麻田散鐵相及上述Cr系碳化物以外之剩餘部分組織,可例舉:肥粒鐵相或殘留沃斯田鐵相、其他析出物(亦包含粒徑未滿2.0 μm之Cr系碳化物)、中介物(例如,Al或Si等之氧化物及Mn等之硫化物等)。剩餘部分組織之體積率較佳為20%以下,更佳為10%以下,進而較佳為5%以下,進而更佳為2%以下。剩餘部分組織之體積率亦可為0%。 再者,由於藉由淬火處理而硬質化,故而於淬火處理鋼板中,洛氏硬度為HRC55以上。Furthermore, in the steel sheet obtained by quenching hot-rolled steel sheet, hot-rolled and annealed steel sheet, cold-rolled steel sheet, and cold-rolled and annealed steel sheet (hereinafter also referred to as quenched steel sheet), the structure system other than Cr-based carbides is called Matian San The organization of the iron phase subject. Specifically, the volume ratio of the Asada scattered iron phase is 80% or more, preferably 90% or more, more preferably 95% or more, and still more preferably 98% or more of the metal structure. The volume ratio of the scattered iron phase of Matian can also be 100%. As the remaining part of the structure other than the Asada iron phase and the aforementioned Cr-based carbides, examples may include: fertilizer grain iron phases, residual austenitic iron phases, and other precipitates (including Cr-based carbides with a particle size of less than 2.0 μm) ), intermediates (for example, oxides such as Al or Si, sulfides such as Mn, etc.). The volume ratio of the remaining part of the tissue is preferably 20% or less, more preferably 10% or less, still more preferably 5% or less, and still more preferably 2% or less. The volume ratio of the remaining part of the tissue can also be 0%. Furthermore, since it is hardened by the quenching treatment, in the quenched steel sheet, the Rockwell hardness is HRC55 or more.
此外,於對淬火處理鋼板實施了回火處理之鋼板(以下,亦稱為回火處理鋼板)中,Cr系碳化物以外之組織與淬火處理後相比,成為位錯密度暨固溶C、N減少之麻田散鐵相(有時稱為回火麻田散鐵相)主體之組織,且大致維持回火處理前之麻田散鐵分率。 具體而言,成為麻田散鐵相之體積率為80%以上、較佳為90%以上、更佳為95%以上、進而較佳為98%以上之金屬組織。又,成為肥粒鐵相之體積率為20%以下、較佳為10%以下、更佳為5%以下、進而較佳為2%以下之金屬組織。作為肥粒鐵相、麻田散鐵相及上述Cr系碳化物以外之剩餘部分組織,可例舉:殘留沃斯田鐵相或其他析出物(亦包含粒徑未滿2.0 μm之Cr系碳化物)、中介物(例如,Al或Si等之氧化物及Mn等之硫化物等)。剩餘部分組織之體積率較佳為5%以下,更佳為2%以下。 此處,進行回火處理,係用以對藉由淬火處理而硬質化之鋼板之硬度及耐久性進行調整,與回火處理前之淬火處理鋼板相比,回火處理鋼板之硬度降低。具體而言,於回火處理鋼板中,洛氏硬度變為HRC40~50。In addition, in the steel sheet subjected to the tempering treatment of the quenched steel sheet (hereinafter also referred to as the tempered steel sheet), the structure other than the Cr-based carbide becomes the dislocation density and solid solution C, The main structure of the Asada scattered iron phase (sometimes called the tempered Asada scattered iron phase) with reduced N, and roughly maintain the Asada scattered iron fraction before the tempering treatment. Specifically, the volume ratio of the Asada scattered iron phase is 80% or more, preferably 90% or more, more preferably 95% or more, and still more preferably 98% or more of the metal structure. In addition, the volume ratio of the ferrous iron phase is 20% or less, preferably 10% or less, more preferably 5% or less, and still more preferably 2% or less of the metallic structure. Examples of the remaining part of the structure other than the ferrous iron phase, the Asada scattered iron phase, and the aforementioned Cr-based carbides include: residual austenitic iron phase or other precipitates (including Cr-based carbides with a particle size of less than 2.0 μm) ), intermediates (for example, oxides such as Al or Si, sulfides such as Mn, etc.). The volume ratio of the remaining part of the tissue is preferably 5% or less, more preferably 2% or less. Here, the tempering treatment is used to adjust the hardness and durability of the steel plate hardened by the quenching treatment. Compared with the quenched steel plate before the tempering treatment, the hardness of the tempered steel plate is lowered. Specifically, in the tempered steel sheet, the Rockwell hardness becomes HRC40-50.
又,粒徑為2.0 μm以上之Cr系碳化物之體積率係依以下方式進行測定。 亦即,自成為試驗材料之鋼板之板寬中央部採集組織觀察用試片。繼而,對試片之軋製方向剖面進行鏡面研磨後,使用苦味酸鹽酸水溶液進行蝕刻,以10個視野拍攝出倍率500倍之光學顯微鏡照片。藉由圖像解析對所獲得之組織照片中之Cr系碳化物之面積進行測定,特定出圓相當直徑為2.0 μm以上之Cr系碳化物。然後,計算所特定之圓相當直徑為2.0 μm以上之Cr系碳化物之合計面積率,將該計算出之值設為粒徑為2.0 μm以上之Cr系碳化物之體積率。 此處,於上述圖像解析中,對於組織照片之數位資料,使用圖像解析裝置,藉由對比度差自動檢測母相(肥粒鐵相或麻田散鐵相)之晶界與析出物之交界(晶界及交界呈現線狀之黑色對比度,晶粒呈現相對較亮之對比度)。其次,將由母相與析出物之交界線所包圍之區域設為析出物,自動測定各析出物之區域之面積。其後,對於藉由下述方法鑑定為Cr系碳化物之析出物,僅特定出面積為3.14 μm2 以上(即,圓相當直徑為2.0 μm以上)者。然後,計算所特定之析出物之合計面積。 然後,求取(圓相當直徑為2.0 μm以上之析出物(Cr系碳化物)之合計面積)÷(組織照片之總面積)×100[%],將所求得之值設為粒徑為2.0 μm以上之Cr系碳化物之體積率。In addition, the volume ratio of Cr-based carbides with a particle size of 2.0 μm or more was measured in the following manner. That is, a test piece for tissue observation was collected from the center of the width of the steel plate used as the test material. Then, after mirror-polishing the section in the rolling direction of the test piece, it was etched with a picric acid aqueous solution, and an optical microscope photograph with a magnification of 500 times was taken with 10 fields of view. The area of the Cr-based carbide in the obtained microstructure photograph was measured by image analysis, and the Cr-based carbide with a circle equivalent diameter of 2.0 μm or more was identified. Then, the total area ratio of Cr-based carbides with a specified circle-equivalent diameter of 2.0 μm or more is calculated, and the calculated value is set as the volume ratio of Cr-based carbides with a particle size of 2.0 μm or more. Here, in the above-mentioned image analysis, for the digital data of the tissue photo, an image analysis device is used to automatically detect the boundary between the grain boundary and the precipitate of the parent phase (the fat iron phase or the Asada iron phase) by the contrast difference (The grain boundaries and junctions present linear black contrast, and the crystal grains present relatively bright contrast). Next, the area surrounded by the boundary line between the parent phase and the precipitate is set as the precipitate, and the area of each precipitate area is automatically measured. After that, for the precipitates identified as Cr-based carbides by the following method, only those with an area of 3.14 μm 2 or more (that is, a circle equivalent diameter of 2.0 μm or more) were identified. Then, calculate the total area of the specified precipitates. Then, calculate (total area of precipitates (Cr-based carbides) with a circle equivalent diameter of 2.0 μm or more) ÷ (total area of microstructure photos) × 100 [%], and set the obtained value as the particle size The volume ratio of Cr-based carbides above 2.0 μm.
又,上述組織照片中之析出物為Cr系碳化物之鑑定係依以下方式進行。 亦即,於拍攝了上述組織照片之相同視野中,進行使用掃描式電子顯微鏡-能量色散X射線光譜法(SEM-EDS,Scanning Electron Microscope-Energy Dispersive X-ray Spectroscopy)之點分析,測定所觀察之析出物之主成分。 具體而言,於析出物中之Cr及Fe之合計含量為60質量%以上,且析出物中之Cr含量相對於析出物中之Fe及Cr之合計含量的比([Cr含量(質量%)]/([Fe含量(質量%)]+[Cr含量(質量%)])為0.4以上之情形時,鑑定該析出物為Cr系碳化物。In addition, the identification of the precipitates in the above-mentioned structure photographs as Cr-based carbides was carried out in the following manner. That is, in the same field of view where the above-mentioned tissue photograph was taken, a point analysis using Scanning Electron Microscope-Energy Dispersive X-ray Spectroscopy (SEM-EDS) was performed to measure the observation The main component of the precipitate. Specifically, the total content of Cr and Fe in the precipitates is 60% by mass or more, and the ratio of the Cr content in the precipitates to the total content of Fe and Cr in the precipitates ([Cr content (mass%) ]/([Fe content (mass %)] + [Cr content (mass %)]) is 0.4 or more, the precipitate is identified as a Cr-based carbide.
此外,肥粒鐵相及麻田散鐵相之體積率係依以下方式求取。 亦即,於上述組織照片中,根據組織形狀及蝕刻強度區別麻田散鐵相與肥粒鐵相(再者,麻田散鐵相係較肥粒鐵相被蝕刻得更深。因此,麻田散鐵相係較肥粒鐵相之對比度更暗)。繼而,藉由圖像處理,針對每個視野分別計算肥粒鐵相及麻田散鐵相之體積率。繼而,計算每個視野所獲得之肥粒鐵相及麻田散鐵相之體積率之算術平均值,將該值設為肥粒鐵相及麻田散鐵相之體積率。In addition, the volume ratios of the ferrous iron phase and the Asada scattered iron phase are calculated in the following way. That is, in the above-mentioned structure photo, the Asada iron phase and the fat iron phase are distinguished according to the structure shape and the etching strength (Furthermore, the Asada iron phase is etched deeper than the fat iron phase. Therefore, the Asada iron phase is etched more deeply than the fat iron phase. The contrast is darker than the fat iron phase). Then, through image processing, the volume ratios of the fat iron phase and the Asada scattered iron phase are calculated for each field of view. Then, calculate the arithmetic mean of the volume ratios of the fat iron phase and the Asada iron phase obtained in each field of view, and set this value as the volume ratio of the fat iron phase and the Asada iron phase.
再者,本發明之一實施形態之不鏽鋼鋼板之厚度並無特別限定,就應用於菜刀或剃刀、醫療用切削用具等之觀點而言,較佳係設為0.1~5.0 mm。本發明之一實施形態之不鏽鋼鋼板之厚度更佳為0.5 mm以上,進而較佳為1.0 mm以上。又,本發明之一實施形態之不鏽鋼鋼板之厚度更佳為4.0 mm以下,進而較佳為2.5 mm以下。Furthermore, the thickness of the stainless steel sheet in one embodiment of the present invention is not particularly limited, but from the viewpoint of application to kitchen knives, razors, medical cutting tools, etc., it is preferably set to 0.1 to 5.0 mm. The thickness of the stainless steel plate in one embodiment of the present invention is more preferably 0.5 mm or more, and still more preferably 1.0 mm or more. In addition, the thickness of the stainless steel sheet in one embodiment of the present invention is more preferably 4.0 mm or less, and still more preferably 2.5 mm or less.
其次,對於本發明之一實施形態之不鏽鋼鋼板之製造方法進行說明。 亦即,藉由轉爐或電爐等熔解爐熔製鋼液。繼而,對於該鋼液實施盛鋼桶精煉或真空精煉之二次精煉,調整為上述成分組成。繼而,藉由連續鑄造法或鑄錠-初軋法等將該鋼液製成鋼素材(鋼坯)。Next, a method of manufacturing a stainless steel sheet according to an embodiment of the present invention will be described. That is, molten steel is melted by a melting furnace such as a converter or an electric furnace. Then, the molten steel is subjected to secondary refining of ladle refining or vacuum refining to adjust the composition to the above-mentioned composition. Then, the molten steel is made into a steel material (slab) by a continuous casting method, an ingot-blooming method, or the like.
・第1步驟(鋼坯加熱步驟) 然後,作為第1步驟,將上述鋼坯於1200~1350℃下保持30分鐘以上。・The first step (slab heating step) Then, as a first step, the above-mentioned steel slab is held at 1200 to 1350°C for 30 minutes or more.
將鋼坯於1200~1350℃下保持30分鐘以上 於熱軋前所進行之鋼坯之加熱中,需要使鑄造時鋼坯剖面之柱狀晶與等軸晶之交界部附近之沿鑄造方向生成之粗大之Cr系碳化物極力固溶於沃斯田鐵相。 此處,若鋼坯之保持溫度(以下,亦稱為鋼坯加熱溫度)未滿1200℃,則無法充分地促進Cr系碳化物固溶於沃斯田鐵相。因此,無法充分地抑制粗大之Cr系碳化物之生成,無法獲得良好之表面品質。另一方面,若鋼坯加熱溫度超過1350℃,則鋼坯之金屬組織成為沃斯田鐵相與δ肥粒鐵相之雙相組織、或δ肥粒鐵之單相組織,無法充分地促進Cr系碳化物固溶於沃斯田鐵相。因此,無法充分地抑制粗大之Cr系碳化物之生成,無法獲得良好之表面品質。 因此,鋼坯加熱溫度設為1200~1350℃之範圍。鋼坯加熱溫度較佳為1300℃以下,更佳為1250℃以下。Keep the billet at 1200~1350℃ for more than 30 minutes In the heating of the billet before hot rolling, it is necessary to make the coarse Cr-based carbides generated along the casting direction near the boundary between the columnar crystals and the equiaxed crystals of the billet section during casting be as solid as possible in the austenitic iron Mutually. Here, if the holding temperature of the slab (hereinafter also referred to as the slab heating temperature) is less than 1200°C, the solid dissolution of the Cr-based carbides in the austenitic iron phase cannot be promoted sufficiently. Therefore, the generation of coarse Cr-based carbides cannot be sufficiently suppressed, and good surface quality cannot be obtained. On the other hand, if the slab heating temperature exceeds 1350°C, the metal structure of the slab becomes a dual-phase structure of austenitic iron phase and δ ferrous iron phase, or a single-phase structure of δ ferrous iron, and the Cr-based structure cannot be sufficiently promoted. The carbides are dissolved in the austenitic iron phase. Therefore, the generation of coarse Cr-based carbides cannot be sufficiently suppressed, and good surface quality cannot be obtained. Therefore, the slab heating temperature is set to the range of 1200 to 1350°C. The slab heating temperature is preferably 1300°C or lower, more preferably 1250°C or lower.
又,於在1200~1350℃下之保持時間未滿30分鐘之情形時,Cr系碳化物固溶於沃斯田鐵相仍不充分。因此,無法充分地抑制粗大之Cr系碳化物之生成,無法獲得良好之表面品質。 因此,於1200~1350℃下之保持時間設為30分鐘以上。 再者,若該保持時間超過24小時,則鋼坯之加熱中所生成之氧化皮變厚,容易產生表面缺陷。又,生產性亦降低。因此,該保持時間較佳係設為24小時以下。該保持時間更佳為12小時以下,進而較佳為3小時以下。In addition, when the retention time at 1200 to 1350°C is less than 30 minutes, the solid dissolution of the Cr-based carbide in the austenitic iron phase is still insufficient. Therefore, the generation of coarse Cr-based carbides cannot be sufficiently suppressed, and good surface quality cannot be obtained. Therefore, the holding time at 1200 to 1350°C is set to 30 minutes or more. Furthermore, if the holding time exceeds 24 hours, the oxide scale generated during the heating of the billet becomes thicker, and surface defects are likely to occur. In addition, productivity is also reduced. Therefore, the retention time is preferably set to 24 hours or less. The retention time is more preferably 12 hours or less, and still more preferably 3 hours or less.
・第2步驟:熱軋步驟 繼而,作為第2步驟,對該鋼坯實施熱軋而製成熱軋鋼板,並捲取該熱軋鋼板。 此時,較為重要的是,熱軋中之軋製道次之中,將結束溫度為1050℃以上且軋縮率為20%以上之軋製道次數量設為3個道次以上,又,將熱軋鋼板之捲取溫度設為600℃以上。・Step 2: Hot rolling step Then, as a second step, the steel billet is hot-rolled to produce a hot-rolled steel sheet, and the hot-rolled steel sheet is coiled. At this time, it is more important that among the rolling passes in the hot rolling, the number of rolling passes with an end temperature of 1050°C or higher and a reduction ratio of 20% or higher is set to 3 passes or more. Set the coiling temperature of the hot-rolled steel sheet to 600°C or higher.
熱軋中之軋製道次之中,結束溫度為1050℃以上且軋縮率為20%以上之軋製道次數量為3個道次以上 於熱軋中,進一步促進Cr系碳化物固溶於沃斯田鐵相,消除鋼坯加熱後所殘留之粗大之Cr系碳化物。又,藉由促進沃斯田鐵相之動態再結晶及/或靜態再結晶,使沃斯田鐵相之晶粒微細化。藉此,於其後之熱軋鋼板之捲取時,自沃斯田鐵相之晶界析出之Cr系碳化物之析出位置增加,從而再析出之Cr系碳化物亦微細化。 尤其是,藉由於1050℃以上之溫度下實施軋製,可有效地促進沃斯田鐵相之動態再結晶及/或靜態再結晶。又,藉由將每個軋製道次之軋縮率設為20%以上,軋製應變可被有效地賦予至鋼坯之板厚中央部。藉此,更加有效地消除於鋼坯之柱狀晶與等軸晶之交界部附近沿鑄造方向所生成之粗大之Cr系碳化物。 因此,於熱軋中之軋製道次之中,需要將結束溫度為1050℃以上且軋縮率為20%以上之軋製道次數量(以下,亦稱為滿足既定條件之軋製道次)設為3個道次以上。 再者,滿足既定條件之軋製道次數量之上限並無特別限定,若過度增加,則為了維持軋製溫度需要大量熱輸入,從而導致製造成本增加,因此,滿足既定條件之軋製道次數量較佳係設為10個道次以下。Among the rolling passes in hot rolling, the number of rolling passes with an end temperature of 1050°C or higher and a reduction ratio of 20% or higher is 3 passes or more In hot rolling, it further promotes the solid dissolution of Cr-based carbides in the austenitic iron phase, and eliminates the coarse Cr-based carbides remaining after the billet is heated. Furthermore, by promoting the dynamic recrystallization and/or static recrystallization of the austenitic iron phase, the crystal grains of the austenitic iron phase are refined. As a result, during the subsequent coiling of the hot-rolled steel sheet, the precipitation positions of the Cr-based carbides precipitated from the grain boundaries of the austenitic iron phase increase, and the re-precipitated Cr-based carbides are also refined. In particular, by rolling at a temperature above 1050°C, the dynamic recrystallization and/or static recrystallization of the austenitic iron phase can be effectively promoted. In addition, by setting the reduction ratio of each rolling pass to 20% or more, the rolling strain can be effectively imparted to the central part of the slab thickness. Thereby, the coarse Cr-based carbides generated along the casting direction in the vicinity of the boundary between the columnar crystals and the equiaxed crystals of the billet can be more effectively eliminated. Therefore, among the rolling passes in hot rolling, the number of rolling passes with a finishing temperature of 1050°C or higher and a reduction ratio of 20% or higher (hereinafter, also referred to as a rolling pass that satisfies the established conditions) is required. ) Set to 3 passes or more. Furthermore, the upper limit of the number of rolling passes that meets the established conditions is not particularly limited. If it is excessively increased, a large amount of heat input is required to maintain the rolling temperature, resulting in an increase in manufacturing costs. Therefore, the rolling passes that meet the established conditions The number is preferably set to 10 passes or less.
又,熱軋中之每個軋製道次之軋縮率之上限並無特別限定,若每個軋製道次之軋縮率過大,則軋製負重增加,軋製變得困難。因此,每個軋製道次之軋縮率較佳為60%以下。 此處,所謂每個軋製道次之軋縮率,係以([該軋製道次開始時之被軋製材之板厚(mm)]-[該軋製道次結束時之被軋製材之板厚(mm)])/[該軋製道次開始時之被軋製材之板厚(mm)]×100之形式而求得者。In addition, the upper limit of the reduction ratio of each rolling pass in hot rolling is not particularly limited. If the reduction ratio of each rolling pass is too large, the rolling load increases and rolling becomes difficult. Therefore, the reduction ratio of each rolling pass is preferably 60% or less. Here, the so-called reduction ratio of each rolling pass is based on ([the thickness of the rolled material at the beginning of the rolling pass (mm)]-[the rolled material at the end of the rolling pass The thickness (mm)])/[the thickness of the rolled material at the beginning of the rolling pass (mm)]×100.
再者,熱軋之軋製道次數量(總數)較佳係設為8~20個道次。又,熱軋通常由粗軋及精軋構成。於該情形時,粗軋之軋製道次數量較佳係設為3~10個道次,精軋之軋製道次數量較佳係設為5~10個道次。又,軋製結束溫度較佳係設為900~1100℃。進而,熱軋中之總軋縮率較佳係設為85.0~99.8%。Furthermore, the number of rolling passes (total) of hot rolling is preferably set to 8-20 passes. In addition, hot rolling usually consists of rough rolling and finish rolling. In this case, the number of rolling passes for rough rolling is preferably set to 3-10 passes, and the number of rolling passes for finishing rolling is preferably set to 5-10 passes. In addition, the rolling end temperature is preferably set to 900 to 1100°C. Furthermore, the total reduction ratio in hot rolling is preferably set to 85.0 to 99.8%.
捲取溫度:600℃以上 於熱軋之精軋後,捲取熱軋鋼板。此時,使沃斯田鐵相變態成肥粒鐵相,將熱軋鋼板之金屬組織作為肥粒鐵相主體之組織。於捲取溫度未滿600℃之情形時,沃斯田鐵相變態成麻田散鐵相,導致鋼板之硬質化。又,存在鋼板之平坦度變差,難以實施以後之步驟之情形。進而,存在鋼板產生淬火裂紋之情形。 因此,捲取溫度設為600℃以上。捲取溫度較佳為650℃以上,更佳為700℃以上,進而較佳為750℃以上。捲取溫度之上限並無特別限定,較佳係設為850℃以下。若捲取溫度超過850℃,則捲取溫度成為沃斯田鐵相與肥粒鐵相之雙相溫度區域。因此,沃斯田鐵相之穩定性變高,自沃斯田鐵相至肥粒鐵相之變態發生延遲。藉此,(捲取之鋼板)於大氣冷卻後且熱軋板退火前,存在沃斯田鐵相變態成硬質之麻田散鐵相之情形。其結果,存在產生熱軋鋼板之明顯硬質化或形狀不良之情形,因此不佳。Coiling temperature: above 600℃ After the finish rolling of the hot rolling, the hot-rolled steel sheet is coiled. At this time, the austenitic iron phase is transformed into a fat iron phase, and the metal structure of the hot-rolled steel sheet is used as the main body of the fat iron phase. When the coiling temperature is less than 600°C, the austenitic iron phase is transformed into a matian scattered iron phase, resulting in hardening of the steel plate. In addition, the flatness of the steel sheet may deteriorate, making it difficult to implement subsequent steps. Furthermore, there are cases where quenching cracks occur in the steel sheet. Therefore, the coiling temperature is set to 600°C or higher. The coiling temperature is preferably 650°C or higher, more preferably 700°C or higher, and still more preferably 750°C or higher. The upper limit of the coiling temperature is not particularly limited, but it is preferably 850°C or lower. If the coiling temperature exceeds 850°C, the coiling temperature becomes the dual phase temperature region of the austenitic iron phase and the fat iron phase. Therefore, the stability of the austenitic iron phase becomes higher, and the transformation from the austenitic iron phase to the fat iron phase is delayed. As a result, after the (coiled steel sheet) is cooled in the atmosphere and before the hot-rolled sheet is annealed, the austenitic iron phase is transformed into a hard Asada scattered iron phase. As a result, the hot-rolled steel sheet may become significantly hardened or have poor shape, which is undesirable.
・第3步驟:熱軋板退火步驟 繼而,作為第3步驟,對依上述方式獲得之熱軋鋼板實施熱軋板退火,並製成熱軋退火鋼板。 於該熱軋板退火中,將保持溫度設為750~900℃,將保持時間設為10分鐘以上。・Step 3: Annealing step of hot rolled sheet Then, as the third step, the hot-rolled steel sheet obtained in the above-mentioned manner is subjected to hot-rolled sheet annealing to form a hot-rolled annealed steel sheet. In this hot-rolled sheet annealing, the holding temperature is set to 750 to 900°C, and the holding time is set to 10 minutes or more.
熱軋板退火之保持溫度:750~900℃ 進行熱軋板退火,係為了抑制加工成切削用具等既定形狀時之裂紋(以下,亦稱為加工裂紋)。並且,於該熱軋板退火中,藉由再結晶,將藉由熱軋所形成之軋製加工組織(包含承受了應變之晶粒之金屬組織)取代為幾乎不包含應變之肥粒鐵相之晶粒。Holding temperature of hot-rolled sheet annealing: 750~900℃ The hot-rolled sheet annealing is performed to suppress cracks (hereinafter also referred to as machining cracks) when processed into a predetermined shape such as a cutting tool. In addition, in the annealing of the hot-rolled sheet, by recrystallization, the rolled structure formed by hot rolling (the metallic structure including the strain-bearing crystal grains) is replaced with a ferrous iron phase containing almost no strain的晶粒。 The grain.
但,若熱軋板退火之保持溫度(以下,亦稱為熱軋板退火溫度)未滿750℃,則會殘留熱軋時所形成之軋製加工組織。結果,熱軋退火鋼板之延展性降低,容易產生加工裂紋。又,若熱軋板退火溫度超過900℃,則晶粒粗大化,韌性降低。結果,容易產生加工裂紋。 因此,熱軋板退火溫度設為750~900℃之範圍。熱軋板退火溫度較佳為800℃以上。又,熱軋板退火溫度較佳為875℃以下,更佳為850℃以下。 再者,熱軋板退火溫度於保持中可固定,又,只要處於上述溫度範圍內,則於保持中,亦可不一直固定。對於以下所說明之冷軋板退火溫度或淬火溫度、回火溫度,亦同樣如此。However, if the holding temperature of the hot-rolled sheet annealing (hereinafter also referred to as the hot-rolled sheet annealing temperature) is less than 750°C, the rolled structure formed during the hot rolling will remain. As a result, the ductility of the hot-rolled and annealed steel sheet is reduced, and processing cracks are prone to occur. In addition, if the annealing temperature of the hot-rolled sheet exceeds 900°C, the crystal grains become coarser and the toughness decreases. As a result, processing cracks are likely to occur. Therefore, the annealing temperature of the hot-rolled sheet is set to the range of 750 to 900°C. The annealing temperature of the hot-rolled sheet is preferably 800°C or higher. In addition, the annealing temperature of the hot-rolled sheet is preferably 875°C or lower, more preferably 850°C or lower. Furthermore, the annealing temperature of the hot-rolled sheet may be fixed during the holding, and as long as it is within the above-mentioned temperature range, the annealing temperature may not always be fixed during the holding. The same is true for the annealing temperature, quenching temperature, and tempering temperature of the cold-rolled sheet described below.
熱軋板退火之保持時間:10分鐘以上 於熱軋板退火之保持時間未滿10分鐘之情形時,無法使鋼板內之材質充分均勻化。因此,熱軋板退火之保持時間設為10分鐘以上。熱軋板退火之保持時間較佳為3小時以上,更佳為6小時以上。再者,於熱軋板退火之保持時間超過96小時之情形時,存在氧化皮變厚,難以進行其後之除氧化皮處理之情形。因此,熱軋板退火之保持時間較佳為96小時以下。又,熱軋板退火之保持時間較佳為24小時以下,更佳為12小時以下。Holding time of hot-rolled sheet annealing: more than 10 minutes When the holding time of the hot-rolled sheet annealing is less than 10 minutes, the material in the steel sheet cannot be sufficiently homogenized. Therefore, the holding time for annealing the hot-rolled sheet is set to 10 minutes or more. The holding time for annealing the hot-rolled sheet is preferably 3 hours or more, more preferably 6 hours or more. Furthermore, when the holding time of the annealing of the hot-rolled sheet exceeds 96 hours, there may be cases where the oxide scale becomes thick and it is difficult to perform the subsequent descaling treatment. Therefore, the holding time for annealing the hot-rolled sheet is preferably 96 hours or less. In addition, the holding time for annealing the hot-rolled sheet is preferably 24 hours or less, more preferably 12 hours or less.
又,於熱軋板退火後,可任意進行作為第4步驟之冷軋,進而進行作為第5步驟之冷軋板退火。In addition, after the hot-rolled sheet is annealed, cold rolling as the fourth step may be arbitrarily performed, and further cold-rolled sheet annealing as the fifth step may be performed.
・第4步驟:冷軋步驟 於第4步驟中,對熱軋板退火後所獲得之熱軋退火鋼板實施冷軋而製成冷軋鋼板。 冷軋之方法並無特別限定,例如,可使用串列軋機或多輥軋機。又,對於冷軋中之軋縮率,亦無特別限定,但就冷軋板退火後之成形性或鋼板之形狀矯正的觀點而言,冷軋中之軋縮率較佳係設為50%以上。又,就避免過度之軋製負重的觀點而言,冷軋中之軋縮率較佳係設為95%以下。・Step 4: Cold rolling step In the fourth step, the hot-rolled annealed steel sheet obtained after the hot-rolled sheet is annealed is cold-rolled to produce a cold-rolled steel sheet. The method of cold rolling is not particularly limited. For example, a tandem mill or a multi-roll mill can be used. In addition, the reduction rate in cold rolling is not particularly limited, but from the viewpoint of the formability of the cold-rolled sheet after annealing or the shape correction of the steel sheet, the reduction rate in cold rolling is preferably set to 50% above. In addition, from the viewpoint of avoiding excessive rolling load, the reduction ratio in cold rolling is preferably set to 95% or less.
・第5步驟:冷軋板退火步驟 於第5步驟(冷軋板退火步驟)中,對冷軋後所獲得之冷軋鋼板實施保持溫度為700~850℃、保持時間為5秒以上之冷軋板退火而製成冷軋退火鋼板。 進行冷軋板退火,主要係為了藉由再結晶去除由冷軋所形成之軋製加工組織。・Step 5: Annealing step of cold rolled sheet In the fifth step (cold-rolled sheet annealing step), the cold-rolled steel sheet obtained after cold rolling is subjected to cold-rolled sheet annealing at a holding temperature of 700 to 850°C and a holding time of 5 seconds or more to produce a cold-rolled annealed steel sheet . Annealing of cold-rolled sheet is mainly for removing the rolling structure formed by cold rolling by recrystallization.
此處,於冷軋板退火之保持溫度(以下,亦稱為冷軋板退火溫度)未滿700℃之情形時,會殘留由冷軋所形成之軋製加工組織,冷軋板退火後所獲得之冷軋退火鋼板之加工性降低。另一方面,若冷軋板退火之保持中之保持溫度超過850℃,則生成沃斯田鐵相,於保持後之冷卻時,沃斯田鐵相變態成麻田散鐵相。因此,導致冷軋板退火後所獲得之冷軋退火鋼板之硬質化及延展性之降低,結果導致加工裂紋。 因此,於進行冷軋板退火之情形時,冷軋板退火溫度設為700~850℃之範圍。冷軋板退火溫度較佳為720℃以上。又,冷軋板退火溫度較佳為830℃以下。Here, when the holding temperature of the cold-rolled sheet annealing (hereinafter also referred to as the cold-rolled sheet annealing temperature) is less than 700°C, the rolled structure formed by cold rolling will remain. The workability of the obtained cold rolled annealed steel sheet is reduced. On the other hand, if the holding temperature during the annealing and holding of the cold-rolled sheet exceeds 850°C, the austenitic iron phase is formed, and upon cooling after the holding, the austenitic iron phase is transformed into the Astian scattered iron phase. Therefore, the hardening and ductility of the cold-rolled annealed steel sheet obtained after the cold-rolled sheet annealing is caused, resulting in processing cracks. Therefore, in the case of performing cold-rolled sheet annealing, the cold-rolled sheet annealing temperature is set in the range of 700 to 850°C. The annealing temperature of the cold-rolled sheet is preferably 720°C or higher. In addition, the annealing temperature of the cold-rolled sheet is preferably 830°C or less.
又,於冷軋板退火之保持時間未滿5秒之情形時,會殘留由冷軋所形成之軋製加工組織,冷軋板退火後所獲得之冷軋退火鋼板之加工性降低。因此,於進行冷軋板退火之情形時,冷軋板退火之保持時間設為5秒以上。冷軋板退火之保持時間較佳為15秒以上。 另一方面,若冷軋板退火之保持時間超過24小時,則存在晶粒粗大化,導致加工裂紋之情形。因此,冷軋板退火之保持時間較佳係設為24小時以下。冷軋板退火之保持時間更佳為15分鐘以下。In addition, when the holding time of the cold-rolled sheet annealing is less than 5 seconds, the rolled structure formed by cold rolling will remain, and the workability of the cold-rolled annealed steel sheet obtained after the cold-rolled sheet annealing will be reduced. Therefore, when performing cold-rolled sheet annealing, the holding time of cold-rolled sheet annealing is set to 5 seconds or more. The holding time of cold-rolled sheet annealing is preferably 15 seconds or more. On the other hand, if the holding time of the cold-rolled sheet annealing exceeds 24 hours, the crystal grains may become coarser, causing processing cracks. Therefore, the holding time of the cold-rolled sheet annealing is preferably set to 24 hours or less. The holding time of cold-rolled sheet annealing is more preferably 15 minutes or less.
・第6步驟:淬火處理步驟 將依上述方式獲得之熱軋退火鋼板、冷軋鋼板或冷軋退火鋼板例如加工成既定形狀後,作為第6步驟,可進而實施保持溫度為950~1200℃、保持時間為5秒~30分鐘、保持後之平均冷卻速度為1℃/秒以上之淬火處理,而製成淬火處理鋼板。・Step 6: Quenching treatment step After processing the hot-rolled annealed steel sheet, cold-rolled steel sheet or cold-rolled annealed steel sheet obtained in the above manner, for example, into a predetermined shape, as the sixth step, a holding temperature of 950 to 1200°C and a holding time of 5 seconds to 30 minutes can be carried out. , Quenching treatment with an average cooling rate of 1°C/sec or more after maintenance, to produce a quenched steel plate.
若淬火處理之保持溫度(以下,亦稱為淬火溫度)未滿950℃,則於淬火處理中之加熱及保持時,未充分地生成沃斯田鐵相,未進行充分之淬火。若淬火溫度超過1200℃,則於淬火處理中之加熱及保持時,存在金屬組織中生成δ肥粒鐵相而未充分地進行淬火之情形。又,存在晶粒明顯粗大化,而於冷卻時產生淬火裂紋或加工裂紋之情形。 因此,淬火溫度設為950~1200℃之範圍。淬火溫度較佳為1000℃以上。又,淬火溫度較佳為1150℃以下。If the holding temperature of the quenching treatment (hereinafter also referred to as the quenching temperature) is less than 950°C, the austenitic iron phase is not sufficiently formed during heating and holding in the quenching treatment, and sufficient quenching is not performed. If the quenching temperature exceeds 1200°C, during the heating and holding during the quenching treatment, there is a case where the δ ferrite phase is formed in the metal structure and the quenching is not sufficiently performed. In addition, the crystal grains are remarkably coarsened, and quenching cracks or processing cracks may occur during cooling. Therefore, the quenching temperature is set in the range of 950 to 1200°C. The quenching temperature is preferably 1000°C or higher. In addition, the quenching temperature is preferably 1150°C or lower.
又,若淬火處理之保持時間未滿5秒,則於加熱及保持時,未充分地生成沃斯田鐵相,且未進行充分之淬火。另一方面,若淬火處理中之保持時間超過30分鐘,則存在晶粒發生粗大化,而產生加工裂紋之情形。 因此,淬火處理之保持時間設為5秒~30分鐘之範圍。淬火處理中之保持時間較佳為15秒以上。又,淬火處理中之保持時間較佳為300秒以下,更佳為120秒以下。In addition, if the holding time of the quenching treatment is less than 5 seconds, the austenitic iron phase is not sufficiently formed during heating and holding, and sufficient quenching is not performed. On the other hand, if the holding time in the quenching treatment exceeds 30 minutes, the crystal grains may be coarsened and processing cracks may occur. Therefore, the holding time of the quenching treatment is set in the range of 5 seconds to 30 minutes. The holding time in the quenching treatment is preferably 15 seconds or more. In addition, the holding time in the quenching treatment is preferably 300 seconds or less, more preferably 120 seconds or less.
進而,於淬火處理中之保持後進行冷卻。於該冷卻時之平均冷卻速度、具體而言自淬火溫度至400℃之平均冷卻速度未滿1℃/秒之情形時,由於加熱時所生成之沃斯田鐵相變態成肥粒鐵相而不是麻田散鐵相,故而未進行充分之淬火。 因此,淬火處理中之保持後之平均冷卻速度設為1℃/秒以上。淬火處理中之保持後之平均冷卻速度較佳為5℃/秒以上,更佳為10℃/秒以上。淬火處理中之保持後之平均冷卻速度之上限並無特別限定,若進行過度之驟冷,則存在發生鋼板形狀變差或產生淬火裂紋之情形。因此,淬火處理中之保持後之平均冷卻速度較佳係設為1000℃/秒以下。Furthermore, it is cooled after being held in the quenching treatment. When the average cooling rate during this cooling, specifically the average cooling rate from the quenching temperature to 400°C, is less than 1°C/sec, the austenitic iron phase generated during heating is transformed into a fat iron phase. It is not the iron phase of Asada scattered, so it has not been quenched sufficiently. Therefore, the average cooling rate after holding in the quenching treatment is set to 1°C/sec or more. The average cooling rate after the retention in the quenching treatment is preferably 5°C/sec or more, more preferably 10°C/sec or more. The upper limit of the average cooling rate after holding in the quenching treatment is not particularly limited. If excessive quenching is performed, the shape of the steel sheet may deteriorate or quenching cracks may occur. Therefore, the average cooling rate after the retention in the quenching treatment is preferably set to 1000°C/sec or less.
再者,冷卻之方法並無特別限定,可使用空氣冷卻、氣體噴射冷卻、霧狀水冷卻、輥冷卻、水浸漬、模具冷卻等各種方法。Furthermore, the method of cooling is not particularly limited, and various methods such as air cooling, gas jet cooling, mist water cooling, roll cooling, water immersion, and mold cooling can be used.
・第7步驟:回火處理步驟 繼而,為了調整硬度及耐久性,作為第7步驟,可對上述淬火處理鋼板進而實施保持溫度為100~800℃、保持時間為5分鐘以上之回火處理,而製成回火處理鋼板。・Step 7: Tempering treatment steps Then, in order to adjust the hardness and durability, as a seventh step, the quenched steel sheet may be further subjected to tempering treatment with a holding temperature of 100 to 800° C. and a holding time of 5 minutes or more to produce a tempered steel sheet.
於回火處理之保持溫度(以下,亦稱為回火溫度)未滿100℃之情形時,麻田散鐵相中之位錯之回復明顯變慢。因此,於回火處理中,難以充分地獲得目標之軟質化效果。另一方面,若回火溫度超過800℃,則麻田散鐵相再次變態成沃斯田鐵相,於保持後之冷卻時,再次變態成麻田散鐵相而硬質化。因此,於回火處理中,難以充分地獲得目標之軟質化效果。 因此,回火溫度設為100~800℃之範圍。回火溫度較佳為200℃以上,更佳為400℃以上。又,回火溫度較佳為750℃以下,更佳為700℃以下。When the holding temperature of the tempering treatment (hereinafter also referred to as the tempering temperature) is less than 100°C, the recovery of dislocations in the scattered iron phase of Asada slows down significantly. Therefore, in the tempering treatment, it is difficult to sufficiently obtain the targeted softening effect. On the other hand, if the tempering temperature exceeds 800°C, the Asada iron phase is transformed into an austenitic iron phase again, and when it is cooled after being maintained, it is transformed into an Asada iron phase and hardened again. Therefore, in the tempering treatment, it is difficult to sufficiently obtain the targeted softening effect. Therefore, the tempering temperature is set in the range of 100 to 800°C. The tempering temperature is preferably 200°C or higher, more preferably 400°C or higher. In addition, the tempering temperature is preferably 750°C or lower, more preferably 700°C or lower.
又,若回火處理之保持時間(以下,亦稱為回火時間)未滿5分鐘,則麻田散鐵相中之位錯之回復變得不充分。因此,於回火處理中,難以充分地獲得目標之軟質化效果。因此,回火時間設為5分鐘以上。回火時間較佳為10分鐘以上,更佳為15分鐘以上。 再者,回火時間越長,硬度越有降低之趨勢,但若回火時間超過60分鐘,則硬度大致固定。因此,回火時間較佳係設為60分鐘以下。回火時間更佳為50分鐘以下,進而較佳為40分鐘以下。In addition, if the holding time of the tempering treatment (hereinafter also referred to as the tempering time) is less than 5 minutes, the recovery of dislocations in the Asada scattered iron phase becomes insufficient. Therefore, in the tempering treatment, it is difficult to sufficiently obtain the targeted softening effect. Therefore, the tempering time is set to 5 minutes or more. The tempering time is preferably 10 minutes or more, more preferably 15 minutes or more. Furthermore, the longer the tempering time, the more the hardness will decrease, but if the tempering time exceeds 60 minutes, the hardness will be roughly constant. Therefore, the tempering time is preferably set to 60 minutes or less. The tempering time is more preferably 50 minutes or less, and still more preferably 40 minutes or less.
再者,關於上述以外之條件,按照慣例即可。 又,例如可於熱軋步驟、熱軋板退火步驟、冷軋步驟、冷軋板退火步驟、淬火步驟及回火步驟之後等任意地進行酸洗處理或噴珠除鏽或表面研削等。進而,可根據用途,於熱軋步驟、熱軋板退火步驟、冷軋板退火步驟、淬火處理步驟、及回火處理步驟之後等實施調質軋製。 並且,使用依上述方式獲得之鋼板,可獲得菜刀或剪刀、醫療用手術刀等切削用具、餐桌用之刀或叉、匙等刀具暨鑷子等精密工具。 [實施例]Furthermore, regarding the conditions other than the above, it is sufficient to follow the usual practice. In addition, for example, the hot rolling step, the hot-rolled sheet annealing step, the cold rolling step, the cold-rolled sheet annealing step, the quenching step, and the tempering step can be arbitrarily performed pickling treatment, bead spraying, rust removal, or surface grinding. Furthermore, depending on the application, temper rolling may be performed after the hot rolling step, the hot-rolled sheet annealing step, the cold-rolled sheet annealing step, the quenching treatment step, and the tempering treatment step. In addition, by using the steel plate obtained in the above manner, cutting tools such as kitchen knives or scissors, medical scalpels, knives such as knives or forks, spoons for table use, and precision tools such as tweezers can be obtained. [Example]
藉由利用容量為150 ton之轉爐所進行之精煉及利用強攪拌-真空氧脫碳處理(SS-VOD)所進行之精煉,熔製具有表1所示之成分組成之鋼(剩餘部分為Fe及不可避免之雜質),藉由連續鑄造,製成寬度為1000 mm、厚度為200 mm之鋼坯。 將該鋼坯保持於表2記載之條件下後,於表2及3記載之條件下實施熱軋及熱軋板退火,並製成熱軋退火鋼板。再者,熱軋之(合計)道次數量均設為14個道次。又,由於熱軋中之第1~5個道次之結束溫度高於第6個道次之結束溫度,故而於表2中省略了記載。此外,表2中亦省略了記載熱軋中之第9個道次以後之結束溫度。 繼而,對於一部分熱軋退火鋼板,進而,於表3記載之條件下,實施冷軋及/或冷軋板退火,並獲得冷軋鋼板及/或冷軋退火鋼板。 對於如此獲得之熱軋退火鋼板、冷軋鋼板及冷軋退火鋼板,藉由上述方法進行金屬組織之觀察,鑑定金屬組織。將結果示於表4。但,於No.35中,於熱軋鋼板之捲取時,由於產生了裂紋,故而未進行金屬組織之鑑定、及其後之評價。By refining by a converter with a capacity of 150 ton and refining by strong stirring-vacuum oxygen decarburization (SS-VOD), the steel with the composition shown in Table 1 is melted (the remainder is Fe And unavoidable impurities), by continuous casting, a billet with a width of 1000 mm and a thickness of 200 mm is made. After the steel slab was kept under the conditions described in Table 2, hot rolling and hot-rolled sheet annealing were performed under the conditions described in Tables 2 and 3 to form a hot-rolled annealed steel sheet. Furthermore, the number of (total) passes of hot rolling is set to 14 passes. In addition, since the end temperature of the 1st to 5th passes in hot rolling is higher than the end temperature of the 6th pass, the description in Table 2 is omitted. In addition, in Table 2, the end temperature after the 9th pass in hot rolling is also omitted. Then, for some of the hot-rolled and annealed steel sheets, cold-rolled and/or cold-rolled sheet annealing was performed under the conditions described in Table 3 to obtain cold-rolled steel sheets and/or cold-rolled annealed steel sheets. For the hot-rolled annealed steel sheet, cold-rolled steel sheet, and cold-rolled annealed steel sheet obtained in this way, the metal structure was observed by the above-mentioned method, and the metal structure was identified. The results are shown in Table 4. However, in No. 35, due to the occurrence of cracks during the coiling of the hot-rolled steel sheet, the identification of the metal structure and subsequent evaluation were not performed.
又,將依上述方式獲得之熱軋退火鋼板、冷軋鋼板及冷軋退火鋼板沖切加工成軋製方向:300 mm×寬度方向:50 mm。然後,於淬火溫度為1050℃、保持時間為15分鐘、自保持後之淬火溫度至400℃之平均冷卻速度為5℃/s之條件下,藉由空氣冷卻,對加工後之鋼板實施了淬火處理。 再者,No.1A及3A-1、3A-2係對淬火處理後之No.1及3之鋼板進而於表3記載之條件下進行了回火處理而獲得者(回火處理鋼板)。In addition, the hot-rolled annealed steel sheet, cold-rolled steel sheet, and cold-rolled annealed steel sheet obtained in the above-mentioned manner are punched into a rolling direction: 300 mm × width direction: 50 mm. Then, under the conditions of a quenching temperature of 1050°C, a holding time of 15 minutes, and an average cooling rate of 5°C/s from the quenching temperature after the holding to 400°C, the processed steel plate was quenched by air cooling. deal with. In addition, No. 1A, 3A-1, and 3A-2 are obtained by tempering the steel plates of No. 1 and 3 after the quenching treatment under the conditions described in Table 3 (tempered steel plates).
對於如此獲得之淬火處理鋼板及回火處理鋼板,藉由上述方法進行金屬組織之觀察,鑑定金屬組織。將結果一併記載於表4。For the quenched steel sheet and tempered steel sheet thus obtained, the metal structure was observed by the above-mentioned method, and the metal structure was identified. The results are shown in Table 4 together.
又,藉由以下之要點,進行硬度及表面品質之評價。 再者,使用淬火處理鋼板進行硬度之評價。但,於進行了回火處理之No.1A及3A-1、3A-2中,對於回火處理後之鋼板,亦進行硬度之評價。 又,使用最終獲得之鋼板進行表面品質之評價,即,於No.1~37中,使用淬火處理鋼板進行表面品質之評價,於No.1A及3A-1、3A-2中,使用回火處理鋼板進行表面品質之評價。In addition, the hardness and surface quality were evaluated based on the following points. Furthermore, the hardened steel plate was used to evaluate the hardness. However, in No. 1A and 3A-1, 3A-2 that have been tempered, the hardness of the steel plate after tempering is also evaluated. In addition, the surface quality of the finally obtained steel plate is evaluated, that is, in No. 1 to 37, the surface quality of the quenched steel plate is used to evaluate the surface quality, and in No. 1A, 3A-1, and 3A-2, tempering is used. The surface quality of the processed steel plate is evaluated.
<硬度之評價> 於依上述方式獲得之鋼板之軋製面中,於任意5個點進行依據JIS Z 2245(2016年)之洛氏硬度試驗,求取該5個點之洛氏硬度之平均值。再者,鋼板之軋製面於試驗前藉由#400之耐水金剛砂研磨紙進行了表面研磨。然後,藉由以下基準,進行硬度之評價。將評價結果一併記載於表4。 ・於未進行回火處理之情形時 ○(合格):洛氏硬度之平均值為HRC55以上 ╳(不合格):洛氏硬度之平均值未滿HRC55 ・於進行回火處理之情形時 ○(合格):回火處理前之洛氏硬度之平均值為HRC55以上,且回火處理後之洛氏硬度之平均值為HRC40以上 ╳(不合格):回火處理前之洛氏硬度之平均值未滿HRC55,或回火處理後之洛氏硬度之平均值未滿HRC40<Evaluation of hardness> In the rolled surface of the steel sheet obtained in the above manner, a Rockwell hardness test according to JIS Z 2245 (2016) is performed at any 5 points, and the average value of the Rockwell hardness of the 5 points is obtained. Furthermore, the rolled surface of the steel plate was surface-polished with #400 water-resistant emery paper before the test. Then, the hardness was evaluated based on the following criteria. The evaluation results are listed in Table 4 together. ・When tempering has not been performed ○(Pass): The average Rockwell hardness is above HRC55 ╳(Unqualified): The average value of Rockwell hardness is less than HRC55 ・In the case of tempering ○ (Pass): The average Rockwell hardness before tempering is HRC55 or more, and the average Rockwell hardness after tempering is HRC40 or more ╳(Unqualified): The average Rockwell hardness before tempering is less than HRC55, or the average Rockwell hardness after tempering is less than HRC40
<表面品質之評價> 自依上述方式獲得之鋼板採集10片軋製方向:100 mm×寬度方向:50 mm之試片。繼而,如圖3所示,針對各試片,對與軋製方向及寬度方向平行之一個端面以相對於寬度方向成3.5°之角度實施了切削加工。繼而,以#400→#600→#800→#1200→#2000之耐水金剛砂紙之順序對切削面進行濕式交叉研磨(以與上一粒度號之研磨方向呈直角方向上進行下一粒度號之研磨的研磨),藉此設置有開刃研磨面。 然後,目測觀察該開刃研磨面,並藉由以下基準,進行表面品質之評價。將評價結果一併記載於表4。 ○(合格):於所有10片試片中,於開刃研磨面未觀察到長度為2.0 mm以上之條紋圖案。 ╳(不合格):於10片試片之至少1片中,於開刃研磨面觀察到長度為2.0 mm以上之條紋圖案。<Evaluation of surface quality> Collect 10 test pieces with rolling direction: 100 mm × width direction: 50 mm from the steel plate obtained by the above method. Then, as shown in FIG. 3, for each test piece, one end surface parallel to the rolling direction and the width direction was cut at an angle of 3.5° with respect to the width direction. Then, in the order of #400→#600→#800→#1200→#2000 water-resistant emery paper, the cutting surface is wet cross-polished (the next grit size is carried out at a right angle to the grinding direction of the previous grit size The grinding of grinding), thereby providing an edged grinding surface. Then, the edged polished surface was visually observed, and the surface quality was evaluated based on the following criteria. The evaluation results are listed in Table 4 together. ○ (Pass): In all 10 test pieces, no stripe pattern with a length of 2.0 mm or more was observed on the bladed polished surface. ╳(Unqualified): In at least one of the 10 test pieces, a stripe pattern with a length of 2.0 mm or more is observed on the bladed grinding surface.
[表1]
[表2]
[表3]
[表4]
如表4所示,於發明例中,均具有較高硬度,且可獲得良好之表面品質。 另一方面,於比較例之No.30、33及34中,由於熱軋中之滿足既定條件之軋製道次數量未滿3個道次,故而粒徑為2.0 μm以上之Cr系碳化物之合計體積率超過10%。因此,無法獲得良好之表面品質。 於No.31中,由於鋼坯加熱溫度超過適當範圍,故而粒徑為2.0 μm以上之Cr系碳化物之合計體積率超過10%。因此,無法獲得良好之表面品質。 於No.32中,由於鋼坯加熱溫度未滿足適當範圍,故而粒徑為2.0 μm以上之Cr系碳化物之合計體積率超過10%。因此,無法獲得良好之表面品質。 於No.35中,由於熱軋之捲取溫度未滿足適當範圍,故而熱軋鋼板產生了裂紋。 於No.36及37中,由於C含量未滿足適當範圍,故而淬火處理後之硬度未滿足適當範圍。再者,於No.36中,由於C含量未滿足適當範圍,故而雖然熱軋中之滿足既定條件之軋製道次數量未滿3個道次,但粒徑為2.0 μm以上之Cr系碳化物之合計體積率為10%以下。As shown in Table 4, all of the invention examples have higher hardness and good surface quality can be obtained. On the other hand, in No. 30, 33, and 34 of the comparative example, since the number of rolling passes meeting the predetermined conditions in the hot rolling is less than 3 passes, the Cr-based carbides with a grain size of 2.0 μm or more The total volume rate exceeds 10%. Therefore, a good surface quality cannot be obtained. In No. 31, because the billet heating temperature exceeds the appropriate range, the total volume ratio of Cr-based carbides with a particle size of 2.0 μm or more exceeds 10%. Therefore, a good surface quality cannot be obtained. In No. 32, because the billet heating temperature did not meet the appropriate range, the total volume ratio of Cr-based carbides with a particle size of 2.0 μm or more exceeded 10%. Therefore, a good surface quality cannot be obtained. In No. 35, because the coiling temperature of hot rolling did not meet the proper range, cracks occurred in the hot rolled steel sheet. In Nos. 36 and 37, since the C content did not meet the appropriate range, the hardness after quenching did not meet the appropriate range. Furthermore, in No. 36, since the C content does not meet the appropriate range, although the number of rolling passes meeting the predetermined conditions in the hot rolling is less than 3 passes, the Cr-based carbonization with a grain size of 2.0 μm or more The total volume rate of objects is 10% or less.
再者,為了參考起見,將可獲得良好之表面品質之發明例之No.1的與軋製方向平行之剖面之光學顯微鏡組織照片示於圖1。又,將無法獲得良好之表面品質之比較例之No.30的與軋製方向平行之剖面之光學顯微鏡組織照片示於圖2。 (產業上之可利用性)Furthermore, for reference, an optical microscope structure photograph of a cross-section parallel to the rolling direction of No. 1 of the invention examples that can obtain a good surface quality is shown in FIG. 1. In addition, an optical microscope structure photograph of a cross-section parallel to the rolling direction of Comparative Example No. 30 in which no good surface quality can be obtained is shown in FIG. 2. (Industrial availability)
本發明之不鏽鋼鋼板由於具有較高之硬度及良好之表面品質,故而可較佳地用於菜刀或剪刀、醫療用手術刀等切削用具、餐桌用之刀或叉、匙等刀具暨鑷子等精密工具之材料。Because the stainless steel plate of the present invention has high hardness and good surface quality, it can be preferably used for cutting tools such as kitchen knives or scissors, medical scalpels, knives, forks, spoons, etc., and tweezers, etc. The material of the tool.
圖1係發明例之No.1之光學顯微鏡組織照片。 圖2係比較例之No.30之光學顯微鏡組織照片。 圖3係表示表面品質之評價中對試片實施切削加工時之狀態之示意圖。Fig. 1 is an optical microscope structure photograph of No. 1 of the invention example. Fig. 2 is an optical microscope photo of No.30 of the comparative example. Fig. 3 is a schematic diagram showing the state when cutting the test piece in the evaluation of the surface quality.
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KR101356919B1 (en) | 2011-12-23 | 2014-01-28 | 주식회사 포스코 | Martensite stainless steel with good hardness and high corrosion resistance and manufacturing method using the same |
KR101463310B1 (en) | 2012-12-20 | 2014-11-19 | 주식회사 포스코 | Martensitic stainless steel and method of the manufacture the same containing 0.4~0.5% carbon |
JP6029662B2 (en) * | 2013-12-09 | 2016-11-24 | 新日鐵住金株式会社 | Austenitic stainless steel sheet and manufacturing method thereof |
WO2016190396A1 (en) * | 2015-05-26 | 2016-12-01 | 新日鐵住金株式会社 | Steel sheet and method for producing same |
JP6600996B2 (en) * | 2015-06-02 | 2019-11-06 | 日本製鉄株式会社 | High carbon steel sheet and method for producing the same |
CN108642408B (en) * | 2018-07-10 | 2019-11-01 | 中国科学院金属研究所 | A kind of high carbon and chromium martensitic stainless steel and preparation method thereof |
-
2021
- 2021-04-07 CN CN202180030734.2A patent/CN115461481B/en active Active
- 2021-04-07 KR KR1020227034500A patent/KR20220147135A/en unknown
- 2021-04-07 WO PCT/JP2021/014829 patent/WO2021220754A1/en unknown
- 2021-04-07 MX MX2022013630A patent/MX2022013630A/en unknown
- 2021-04-07 JP JP2021540467A patent/JP7226564B2/en active Active
- 2021-04-07 US US17/995,582 patent/US20230212705A1/en active Pending
- 2021-04-07 EP EP21797895.6A patent/EP4144882A1/en active Pending
- 2021-04-23 TW TW110114627A patent/TWI774333B/en active
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KR20220147135A (en) | 2022-11-02 |
TWI774333B (en) | 2022-08-11 |
CN115461481A (en) | 2022-12-09 |
WO2021220754A1 (en) | 2021-11-04 |
JPWO2021220754A1 (en) | 2021-11-04 |
CN115461481B (en) | 2024-03-12 |
MX2022013630A (en) | 2023-01-24 |
US20230212705A1 (en) | 2023-07-06 |
JP7226564B2 (en) | 2023-02-21 |
EP4144882A1 (en) | 2023-03-08 |
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