201233990 六、發明說明： 【發明所屬之技術領域】 本發明是有關於一種預 a丨《古關认 ^ 柯連讀鋼胚品質的方法，且牯 別疋有關於-種預_鑄 ㈣W且特 法。 巧胚疋否具有表面橫向裂縫的方 【先前技術】 在煉鋼的生產製程中， 連續鑄造方式來生產鋼胚，生產效率，通常會以 般稱之為連缚鋼胚。在連__ ^式生產之鋼胚— 向裂縫，其中表面橫向裂縫係:見之缺陷有表面横 連鑄鋼胚之寬度方向延展的細面上’沿著 因在於連鎊過程中，連鑄鋼3 =起此缺陷之原 身所能承受的上限，因而在表面上;成二超^ 中，在於:於生產冷卻過程 s界析出而呈現網狀分布的大量 如處於上㈣鋼胚於生產冷卻過財進行拉伸變形(例 之鋼胚上表面)，則上述析出物會使應 變速^時，、詩:界’㈣是在處於如續直過程中之低應 =時：：機構主要為晶界滑移’故應變更易集中於 二的曰裂縫而產生沿著晶界分布的空孔，進㈣成網狀連 主要技術中，為了避免上述表面橫向裂縫缺陷， [S1 度，藉二僻二f:第一種方式為提高連鱗鋼胚之矮直溢 避免連鱗鋼胚在形成網狀連結裂縫的溫度區間拉 4 201233990 伸應變。第二種方式為改變合金成分設計，藉此控制有害 的析出物。 - 然而，在合金成分設計部分，習知技術係以合金添加 量做為評估連鑄鋼胚之高溫延展性以及是否產生表面橫向 裂縫（橫向裂敏感性）之指標。上述評估指標之缺點在於， 橫向裂敏感性與合金添加量之關係通常呈現平滑曲線，缺 乏明確界定高/低橫向裂敏感性的臨界區間，故在實際生產 管理上，難以制定合宜的管制標準。 此外，在相同合金添加量之條件下，其中所對應之橫 • 向裂敏感性分布範圍較廣，表示單一成分之含量對於橫向 裂敏感性的解釋能力偏低，同樣難以制定合宜的管制標準。 另外，在習知技術中，更進一步改以析出物組成元素 含量之乘積做為評估連鑄鋼胚是否產生表面橫向裂縫的指 標。以鋁脫氧鋼為例，析出物為氮化鋁（A1N)，故其組成元 素為銘及氮，因此採用I呂及氮含量的乘積做為評估橫向裂 敏感性的指標。然而，由於I呂及氮含量的乘積與氮化銘之 析出量並非一對一之對應關係，故鋁及氮含量的乘積並不 鲁 適合做為評估連鑄鋼胚是否產生表面橫向裂縫的指標。 【發明内容】 因此，本發明之目的係在提供一種預測連鑄鋼胚是否 具有表面橫向裂縫的方法，其具有可明確界定高/低橫向裂 敏感性的臨界區間，故在實際生產管理上，其適用於制定 . 合宜的管制標準。 根據本發明之一實施例，提供一種預測連鑄鋼胚是否 5 201233990 裂縫的方法，包含:根據多個歷史鋼液之纪 成，刀的3 I以及熱力學原理，計算由此些歷史鋼液鎮造 =夕固歷史連鑄鋼胚中每—個所包含之至少 並：一析出物之含量相加以獲得對 連‘ 鋼胚的f個第-析出物總量，其中每個歷史鋼液 =含里心在特定成分規格的範圍t ;檢測每個歷史連 鑄鋼胚，以獲得多個歷史連鑄鋼胚對應於上述多個第一析 =總量的多個表面橫向裂縫指標； .==之多個第一析出物總量歸納出，對應= ί值H 不會產生表面橫向裂縫之析出物總量臨 ^供鋼液’其中此鋼液之組成成分的含量係落在上 述特定成分規格之範圍中；定量分析上述鋼液，藉以獲得 :::組成成分的含量；以鋼液之組成成分的含量以及孰 力子原理計异’由此鋼液鑄造之連_胚所包含之至少二 =物之3 $ ’並將二析出物之含量相加以獲得對應於此 連每鋼胚之第二析出物總量；比較第二析出物總量是否小 於上述析出物總量臨界值，並獲得檢驗結果；以及當檢驗 、-果為疋時’即預測連鑄鋼胚不具有表面橫向裂縫，故針 對上述連鑄鋼胚進行後處理步驟。 根據本創作之另-實施例，提供一種預測連轉鋼胚是 否具有表面橫向裂縫的方法，包含：根據多個歷史鋼液之 =成成分的含量以及熱力學原理，計算由此些歷史鋼液鑄 多個歷史連禱鋼胚中每一個所包含之至少二析出物之 含篁’並將二析出物之含量相加以獲得對應於此些歷史連 鑄鋼胚的多個第一析出物總量’其中每個歷史鋼液之組成 201233990 3二：1蕙係:落在特定成分規格的範圍中；針對每個歷史 出物總量試驗，以獲得對應於此些第-析 之多個第一展指標；根據此些延展性指標及對應 巧态4析出物總量歸納出，對應於上述多個延展性指 變化之析出物總量臨界值，其中此析出物總量 裂缝的臨界歷史連轉鋼胚是否產生表面橫向 #^^.况，棱仏鋼液，其中此鋼液之組成成分的含 液，藉以定成分規格之範圍中；定量分析上述鋼 的含LG、力分的含量；以鋼液之組成成分 句入 、予原里°十鼻，由此鋼液鑄造之連鑄鋼胚所 二=析出物之含量，並將二析出物之含量相加以 物總鑄鋼胚之第二析出物總量；比較第二析出 果.以Γμ、於上述析出物總量臨界值，並獲得檢驗結 橫向裂縫驗結果為是時，即預測連禱鋼胚不具有表面 、裂縫，故針對該連鑄鋼胚進行後處理步驟。 胚是明之又一實施例’提供一種用於預測連鑄鋼 電：ΐ產=:縫式產品，當電•此 胚是否具有表面=縫:;:如以上所述之預測連鱗鋼 不會產生表面橫向裂縫之析出物總量臨界=歷ί 將此析出物總量臨界值應用於實際生 宜的管制標準’確保所生產之連轉鋼胚的品質。了制疋。 此外，若採用上述與延展性指標相關之預測方法，可 201233990 透過實驗室之拉伸試驗來評估連鑄鋼胚之析出物含量與其 延展性之關係，進而得到連鑄鋼胚之析出物總量與其表面 橫向裂縫之關係。此方法優點在於，不需透過大量生產試 驗之品質評估結果來建立生產流程管制標準，可大量節省 試誤過程之成本。 再者，若採用上述與延展性指標相關之預測方法，在 開發新鋼種時，亦可事先透過實驗室的高溫延展性分析（拉 伸試驗），來評估鋼種成分設計與表面橫向裂縫指標的關 係’進而避開易於產生表面橫向裂的成分區間。 【實施方式】 請參照第1圖，其係繪示根據本發明之一實施例之預 測連鑄鋼胚是否具有表面橫向裂縫的方法的流程圖。預測 連鑄鋼胚是否具有表面橫向裂縫的方法1〇〇(為簡化起見， 以下以「預測方法1〇〇」稱之）開始於步驟102。在步驟102 中，根據多個歷史鋼液之組成成分的含量以及熱力學原 理，來計算由此些歷史鋼液所鑄造之多個歷史連鑄鋼胚中 之析出物的含量，其中每個歷史連鑄鋼胚均包含至少二析 出物，且上述多個歷史鋼液係以一對一方式鑄造出多個歷 史連鑄鋼胚。此外，將每個歷史連鑄鋼胚所包含之至少二 析出物之含量相加，藉以獲得對應於此些歷史連鑄鋼胚之 多個第一析出物總量，亦即每個歷史連鑄鋼胚均具有一特 定之第一析出物總量。其中，每個歷史鋼液之組成成分的 含量係落在特定成分規格的範圍中。 以下即以[M]+[C]=MC之析出反應式來說明如何以熱 201233990 力學原理計算出析出物之含量。當溫度位在起始析出溫度 (Tppt)時，固溶度[M]及[C]以及固溶度積需滿足以下之數學 式·· [M ]〇 x[C ]〇 = 〜’；其中[M]〇及[C]0為起始固溶度， 且A與B為常數。 當溫度降低時，固溶度[M]及[C]以及新的固溶度積必 須滿足以下之數學式，且此新的固溶度積小於上述位在起 始析出溫度時的固溶度積： [M]x[C]^Ae^<[M]^[C]〇 = Ae^..............⑴ 令[M] = [M]「d[M]、[c] = [c]〇— d[c]且綱=聊， 其中d[M]及d[C]分別表示M與c的析出量。 係式，上述第（1)式可簡化如下： ([M]〇’M])x([c] “ [Μ]) = κ ;其中 根據上式可求出Μ的析出量_]，而[M]+[c卜mc之 析出反應式的總析出量為2d[M]’其中2d[M]讀學示 如下： 2d[M] = ([M]0+tC]〇). V^]〇+[C]07-4([M]0[CV^ 由於上述利用熱力學原理計算析出反應式的總析出量 已為此技術領域者所孰知 簡單說明。 …Ή在本說明書中，僅做上述之 此外根據以上所求出之總析出量 之方， j相同剛C]乘積之先決條件下，不同析出階段之MC ^量與M/[C]比值的關係歸納如第2a至％圖。其中， simx表:^析出起始之狀況、第犯圖係用以表示 μ t&m'而第2c圖則用以表示析出終了之狀況。[s] 9 201233990 在第2A至2C圖中，垂直軸之MC析出量係以MC析出量 • 相對於析出量之最大值（最大析出量）之比值來表示， 其中上述MC析出量與最大析出量之比值可稱之為相對析 出分率，而水平軸之[M]/[C]比值中的固溶度[M]及[c]則以 莫耳分率或原子百分比為單位加以計算。由第2A至2C圖 中明顯可以看出’上述之相對析出分率與网/[c]比值並未 存在一對一的對應關係，此外，在相同乘積之情形 下’相對析出分率與[M]/[C]比值有關，且並非定值 。故組 成兀素含量的乘積並*適宜做為評估析$量的指標，亦即 •=以上所述，在[M]+[C]=MC之析出反應式中，M及c含 量的乘積並不適合做為評估連缚鋼胚是否產生表面橫向裂 縫的指標。 方法100繼續進行至步驟201233990 VI. Description of the invention: [Technical field to which the invention pertains] The present invention relates to a method for pre-a 丨 "Gu Gu Guan Ke Ke Lian steel embryo quality, and the screening of the type of pre-cast (four) W and special law. Do you have a surface with a lateral crack? [Prior Art] In the steelmaking process, continuous casting is used to produce steel embryos. The production efficiency is usually called a double-bonded steel embryo. In the steel blast produced by __^ type - to the crack, in which the surface transverse crack system: see the defect on the fine surface extending in the width direction of the surface transversely cast steel embryo' 3 = the upper limit of the original body of this defect, and thus on the surface; in the super-super ^, it is: in the production cooling process s boundary, a large amount of mesh distribution is present, such as in the upper (four) steel embryo in production cooling If the grain is stretched and deformed (for example, the upper surface of the steel embryo), then the above-mentioned precipitates will be shifted, and the poem: (4) is in the case of a low in the process of straightening =: The mechanism is mainly Grain boundary slip 'should change the pores that are easy to concentrate on the two cracks and produce pores along the grain boundary. In the main technique of entering the network, in order to avoid the lateral crack defects on the surface, [S1 degree, borrowing Second f: The first way is to improve the short straight overflow of the continuous scale steel embryo to avoid the continuous strain of the continuous scale steel embryo in the temperature range of the formation of the network joint crack. The second way is to change the alloy composition design to control harmful precipitates. - However, in the alloy composition design section, the conventional technique uses the alloy addition amount as an index for evaluating the high-temperature ductility of the continuous-cast steel blank and whether or not the surface lateral crack (transverse crack sensitivity) is generated. The disadvantage of the above evaluation index is that the relationship between the transverse crack sensitivity and the alloy addition amount usually shows a smooth curve, and there is no critical section that clearly defines the high/low lateral crack sensitivity. Therefore, it is difficult to formulate appropriate control standards in actual production management. In addition, under the condition of the same alloy addition amount, the corresponding transverse crack sensitivity distribution range is wide, indicating that the content of single component has a low explanatory ability for lateral crack sensitivity, and it is also difficult to formulate appropriate regulatory standards. Further, in the prior art, the product of the content of the constituent elements of the precipitate is further changed as an index for evaluating whether or not the transverse casting crack is generated in the continuous casting steel. Taking aluminum deoxidized steel as an example, the precipitate is aluminum nitride (A1N), so its constituent elements are Ming and nitrogen. Therefore, the product of Ilu and nitrogen content is used as an index to evaluate the sensitivity of transverse cracking. However, since the product of Ilu and nitrogen content and the precipitation of nitriding are not one-to-one correspondence, the product of aluminum and nitrogen content is not suitable as an indicator for evaluating whether or not the transverse casting crack occurs in the continuous casting steel. . SUMMARY OF THE INVENTION Accordingly, it is an object of the present invention to provide a method for predicting whether a continuous casting steel ore has a surface transverse crack, which has a critical interval in which the high/low transverse crack sensitivity can be clearly defined, so in actual production management, It applies to the development of appropriate regulatory standards. According to an embodiment of the present invention, there is provided a method for predicting whether a continuous casting steel blank is 5 201233990 crack, comprising: calculating the historical steel liquid town according to the history of a plurality of historical steel liquids, the 3 I of the knife and the thermodynamic principle At least one of each of the steels produced in the historical solid-casting steel embryo is added: the content of one precipitate is added to obtain the total amount of f-first precipitates of the pair of 'steel embryos, wherein each historical steel liquid = containing The heart is in the range of specific composition specifications; each historical continuous casting steel blank is detected to obtain a plurality of historical continuous casting steel blanks corresponding to the plurality of surface lateral crack indexes of the plurality of first analysis = total amount; The total amount of the plurality of first precipitates is summarized, and the corresponding = ί value H does not produce the total amount of precipitates of the surface lateral cracks, and the content of the constituents of the molten steel falls within the above specific composition specifications. Quantitative analysis of the above molten steel, in order to obtain::: the content of the composition; the content of the composition of the molten steel and the principle of the force of the force of the difference - thus the molten steel casting of the _ embryo contains at least two = 3' of the object and the content of the second precipitate Adding to obtain the total amount of the second precipitate corresponding to each of the steel embryos; comparing whether the total amount of the second precipitate is smaller than the critical value of the total amount of the precipitates, and obtaining the test result; and when the test is - when the fruit is ' That is, it is predicted that the continuous casting steel embryo does not have a surface lateral crack, so the post-processing step is performed for the above-mentioned continuous casting steel embryo. According to another embodiment of the present invention, there is provided a method for predicting whether a continuous transfer steel blank has a surface transverse crack, comprising: calculating the historical steel liquid casting according to the content of a plurality of historical molten steels and the thermodynamic principle The yttrium of at least two precipitates contained in each of the plurality of historical prayer steels is added and the contents of the two precipitates are added to obtain a total amount of the plurality of first precipitates corresponding to the historical continuous cast steel embryos. The composition of each of the historical steel liquids 201233990 3 2: 1 蕙 system: falls within the scope of specific composition specifications; for each historical total output test, to obtain a number of first exhibition corresponding to these first analysis The indicator is based on the ductility index and the corresponding total amount of precipitates, and corresponds to the critical value of the total amount of precipitates of the plurality of ductility indicators, wherein the critical history of the total crack of the precipitate is continuous steel Whether the embryo produces surface laterality #^^., 仏 仏 molten steel, wherein the liquid content of the composition of the molten steel, by the range of the composition specifications; quantitative analysis of the content of LG, the force fraction of the above steel; Composition of liquid The composition of the sentence into the original, the ten nose, the molten steel casting of the continuous casting steel embryo = the content of the precipitate, and the content of the two precipitates are added to the total amount of the second precipitate of the total cast steel embryo Comparing the second precipitated fruit. Taking Γμ, the critical value of the total amount of precipitates mentioned above, and obtaining the transverse crack test result of the test junction is YES, that is, it is predicted that the continuous prayer steel embryo has no surface and crack, so the continuous casting steel embryo is Perform post-processing steps. The embryo is a further embodiment of the invention 'providing a method for predicting continuous casting steel: ΐ production =: slotted product, when electricity • whether the embryo has surface = seam:;: as predicted above, the scale steel does not The total amount of precipitates that produce lateral cracks on the surface is critical. The critical value of the total amount of precipitates is applied to the actual control standard to ensure the quality of the continuous steel produced. The system. In addition, if the above-mentioned prediction method related to the ductility index is used, the tensile test of the laboratory can be used to evaluate the relationship between the precipitate content of the continuous casting steel and its ductility, and the total amount of precipitates of the continuous casting steel embryo can be obtained. The relationship with the lateral cracks on the surface. The advantage of this method is that it does not require the quality assessment results of a large number of production tests to establish production process control standards, which can greatly save the cost of the trial and error process. Furthermore, if the above-mentioned prediction method related to the ductility index is used, the relationship between the design of the steel component composition and the surface lateral crack index can be evaluated by the high temperature ductility analysis (tensile test) of the laboratory in advance when developing a new steel grade. 'Further avoid the component intervals that are prone to lateral cracking. [Embodiment] Referring to Figure 1, there is shown a flow chart of a method for predicting whether a continuous casting steel blank has a surface transverse crack according to an embodiment of the present invention. A method for predicting whether a continuous casting steel ore has a lateral transverse crack (hereinafter, referred to as "predictive method 1" for the sake of simplicity) starts at step 102. In step 102, according to the content of the components of the plurality of historical molten steels and the thermodynamic principle, the content of the precipitates in the plurality of historical continuous casting steels cast by the historical steel liquid is calculated, wherein each historical company The cast steel embryos each comprise at least two precipitates, and the plurality of historical steel liquids are cast in a one-to-one manner to produce a plurality of historical continuous cast steel blanks. In addition, the content of at least two precipitates contained in each historical continuous casting steel embryo is added to obtain a total amount of the plurality of first precipitates corresponding to the historical continuous casting steel blanks, that is, each historical continuous casting The steel embryos each have a specific first total amount of precipitates. Among them, the content of each historical molten steel component falls within the range of specific component specifications. The following is a precipitation reaction formula of [M] + [C] = MC to illustrate how to calculate the content of precipitates by the mechanical principle of heat 201233990. When the temperature is at the initial precipitation temperature (Tppt), the solid solubility [M] and [C] and the solid solubility product must satisfy the following mathematical formula: [M ] 〇 x [C ] 〇 = ~ '; [M] 〇 and [C] 0 are the initial solid solubility, and A and B are constant. When the temperature is lowered, the solid solubility [M] and [C] and the new solid solubility product must satisfy the following mathematical formula, and the new solid solubility product is smaller than the above solid solubility at the initial precipitation temperature. Product: [M]x[C]^Ae^<[M]^[C]〇= Ae^..............(1) Let [M] = [M]"d [M], [c] = [c]〇—d[c] and 纲=聊, where d[M] and d[C] represent the precipitation amounts of M and c, respectively, and the above formula (1) It can be simplified as follows: ([M]〇'M])x([c] “[Μ]) = κ ; where the amount of precipitation of Μ can be obtained according to the above formula, and [M]+[c The total precipitation amount of the precipitation reaction formula is 2d[M]', where 2d[M] is read as follows: 2d[M] = ([M]0+tC]〇). V^]〇+[C]07-4 ([M]0[CV^ Since the total precipitation amount of the precipitation reaction formula is calculated by the above-mentioned thermodynamic principle, it has been briefly described by those skilled in the art. Ή In the present specification, only the above is obtained. The relationship between the MC ^ quantity and the M/[C] ratio of different precipitation stages is summarized as the 2a to % graph, and the simx table: ^ is precipitated. The initial situation, the first crime diagram is used to indicate μ t&m' and the 2c graph is used to indicate the end of precipitation. [s] 9 201233990 In the 2A to 2C graph, the MC precipitation amount on the vertical axis is the maximum amount of MC precipitation relative to the precipitation amount ( The ratio of the maximum precipitation amount is expressed by the ratio of the above-mentioned MC precipitation amount to the maximum precipitation amount, which may be referred to as a relative precipitation fraction, and the solid solubility [M] in the [M]/[C] ratio of the horizontal axis and [c] is calculated in units of mole fraction or atomic percentage. It can be clearly seen from the 2A to 2C graphs that there is no one-to-one correspondence between the relative precipitation fraction and the net/[c] ratio. Relationship, in addition, in the case of the same product, the 'relative precipitation fraction is related to the ratio of [M]/[C], and is not fixed. Therefore, the product of the composition of the elementary aliquot and * is suitable as an indicator for evaluating the amount of sputum, That is, == As mentioned above, in the precipitation reaction formula of [M]+[C]=MC, the product of the M and c contents is not suitable as an index for evaluating whether or not the jointed steel embryo produces surface lateral cracks. Go to step
歷史連鑄鋼胚對應於上述多個第一 104。在步驟104中，檢測 鑄鋼胚，藉此獲得上述多個 第一析出物逾官的多個矣而The historical continuous casting steel blank corresponds to the plurality of first 104 described above. In step 104, the cast steel embryo is detected, thereby obtaining a plurality of first precipitates of the plurality of first precipitates
胚是否會產生表面橫向裂Whether the embryo will produce a lateral crack
1歷史連縳她中所包含的的析出物總量 &界值’則表示此歷史連鑄鋼胚中會產生 亦即表不轉造此歷史連鑄鋼胚之歷史鋼液 201233990 的組成成分的含量並不適用於錄造連禱鋼胚，而必須加以 • 調整。相反的，若歷史連鑄鋼胚中所包含的的析出物總量 . 少於析出物總量臨界值，則表示此歷史連鑄鋼胚中並不會 產生表面橫向裂縫，亦即表示鑄造此歷史連鑄鋼胚之歷史 鋼液的組成成分的含量係適用於鑄造連鑄鋼胚。 方法100繼續進行至步驟108。在步驟108中，提供 一鋼液，其中此鋼液的組成成分的含量係落在上述步騾102 之特定成分規格的範圍中。其中，上述之提供一鋼液步驟 可例如為煉鋼生產製程中將製鋼原料融煉成液態的中間製 • 程。 接著進行步驟110，以定量分析步驟108中的鋼液， 藉以獲得此鋼液之組成成分的含量。由於定量分析鋼液之 組成成分含量的方法已為此技術領域者所熟知，故在本說 明書中並未做詳細之說明。 在完成步驟110後，接著進行步驟112，以上述步驟 108所提供之鋼液之組成成分的含量以及熱力學原理，計 算由此鋼液鑄造之連鑄鋼胚中之析出物的含量，其中連鑄 ® 鋼胚包含至少二析出物，且此二析出物係相同於上述每個 歷史連鑄鋼胚所包含之至少二析出物。此外，並將連鑄鋼 胚中之至少二析出物之含量相加，藉此獲得對應於此連鑄 鋼胚之第二析出物總量。 方法100繼續進行至步驟114,以比較連鑄鋼胚之該 第二析出物總量是否小於該上述步驟106所歸納出之析出 物總量臨界值，並獲得檢驗結果。 最後，方法100進行步驟116，當步驟114中之檢驗結 201233990 果為是時，即預測上述連鑄鋼胚應不具有表面橫向裂縫， 故針對上述連鑄鋼胚進行後處理步驟。在特定之實施例 中，上述後處理步驟可包含如軋延製程等煉鋼過程中常見 的製程。 此外，方法100更包含步驟118。在步驟118中，當步 驟114中之檢驗結果為否時，即預測上述連鑄鋼胚應具有 表面橫向裂缝，故針對上述連鑄鋼胚進行補救步驟。在特 定之實施例中，上述之補救步驟可包含如檢驗、研磨及補 銲等常見之措施。 請參照第3圖，其係繪示根據本發明之另一實施例之 預測連鑄鋼胚是否具有表面橫向裂縫的方法的流程圖。預 測連鑄鋼胚是否具有表面橫向裂縫的方法300(為簡化起 見，以下以「預測方法300」稱之）係類似於上述之預測方 法100，其中除步驟304與步驟306之外，其餘之步驟302 及步驟308至步驟318係分別對應顗似於步驟102及步驟 108至步驟118，故其中相關之變化部分即不再加以重複， 以下僅就差異步驟304以及步驟306進行說明。 在步驟304中，針對步驟302中的每個歷史連鑄鋼胚 之試片進行拉伸試驗，以獲得對應於多個第一析出物總量 的多個延展性指標，其中多個第一析出物總量係以一對一 方式與多個延展性指標互相對應。 接著進行步驟306，根據上述多個延展性指標，以及 與上述延展性指標對應的多個第一析出物總量，歸納出對 應於上述多個延展性指標產生急劇變化的析出物總量臨界 值。此外，根據實驗數據顯示，上述析出物總量臨界值係 [s] 12 201233990 對應於步驟302中多個歷史連鑄鋼胚是否產生表面橫向裂 縫之臨界狀況。進一步來說，預測方法100與預測方法300 所分別獲得之析出物總量臨界值具有一致性。 在特定之實施例中，上述預測方法100及300之步驟 102、108、302以及308中之特定成分規格包含如下所示 以重量百分比（wt%)計的多個成分，其中此些成分為： 0.07〜0.17 wt%之碳（C)、1.7 wt%以下之錳（Μη)、0.02 wt% 以下之磷（P)、0.01 wt%以下之硫（S)、0.2〜1.0 wt°/〇之矽（Si)、 0.01 〜0.05 wt%之鋁（A1)、0.01 〜0.1 wt%之鈮(Nb)、0.01 〜0.1 wt%之釩（V)、0.030 wt%以下之鈦（Ti)、0.030 wt%以下之硼 (B)、0.01 wt%以下之氮(N)、不可避免之不純物、以及由鐵 (Fe)所組成之其他部分（殘部）。此外，在此一實施例中，上 述步驟102、108、302以及308中之至少二析出物可為氮 化鋁（A1N)、碳化鈮(NbC)、氮化鈦(TiN)、碳化釩(VC)及氮 化棚(BN)其中任二者。 以下則以實際之實施例更具體地說明本發明，惟本發 明的範圍不受此些實施例之限制。 製備高強度低合金結構用鋼 實施例 首先，提供多個歷史鋼液之組成成分的含量，其中， 每個歷史鋼液之組成成分的含量係落在以下所列示之特定 成分規格的範圍中。此特定成分規格包含以下以wt%計之 多個成分，而此些成分為：0.07〜0.17 wt%之碳、1.2〜1.4 wt% 之錳、0.02 wt%以下之磷、0_008 wt%以下之硫、0.2〜0.4 wt0/〇 之矽、0.01 〜0.05 wt%之鋁、0.01〜0.03 wt%之鈮、0.008 wt% [s] 13 201233990 以下之氮、 分。 不可避免之 不純物、以及由鐵所組成之其他部 献理根ί上述多個歷史鋼液之組成成分的含量以及 胚中每個所包含之憾史連賴 ,,斤出物之含量，並將析出物之含量相 ^ β I巾于、應於此些歷史連鑄鋼胚的多個第一析出物 總I。其甲，歷史造接^ η 丈運“鋼胚所包含析出物為氤化鋁及碳 化鈮，故上述第―姑山此说 3 , 析出物總量即等於氣化I呂及破化銳析出 量之總和。1 Historically, the total amount of precipitates contained in her & boundary value indicates that this historical continuous casting steel embryo will produce the composition of the historical steel liquid 201233990 which is not converted into this historical continuous casting steel embryo. The content does not apply to the construction of a continuous prayer steel, but must be adjusted. On the contrary, if the total amount of precipitates contained in the historical continuous casting steel is less than the critical value of the total amount of precipitates, it means that there is no surface lateral crack in the historical continuous casting steel, which means casting this. The content of the composition of the historical steel liquid of the historical continuous casting steel is suitable for casting continuous casting steel. The method 100 continues with step 108. In step 108, a molten steel is provided, wherein the content of the constituents of the molten steel falls within the range of the specific component specifications of the above step 102. Wherein, the above-mentioned step of providing a molten steel can be, for example, an intermediate process for melting a steel raw material into a liquid state in a steel making process. Next, step 110 is performed to quantitatively analyze the molten steel in step 108 to obtain the content of the constituents of the molten steel. Since the method of quantitatively analyzing the composition of the molten steel is well known to those skilled in the art, it is not described in detail in this specification. After the step 110 is completed, the step 112 is further performed, and the content of the precipitates in the continuous casting steel preform cast by the molten steel is calculated by the content of the constituents of the molten steel provided in the above step 108 and the thermodynamic principle, wherein the continuous casting is performed. ® steel embryos contain at least two precipitates, and the two precipitates are identical to at least two precipitates contained in each of the historical continuous cast steel preforms described above. Further, the contents of at least two precipitates in the continuous casting steel are added, thereby obtaining the total amount of the second precipitate corresponding to the continuous casting steel. The method 100 proceeds to step 114 to compare whether the total amount of the second precipitate of the continuous casting steel is less than the critical value of the total amount of precipitates summarized in the above step 106, and obtain the test result. Finally, the method 100 proceeds to step 116. When the test result 201233990 in step 114 is YES, it is predicted that the continuous casting steel blank should have no surface lateral crack, so the post-processing step is performed on the continuous casting steel embryo. In a particular embodiment, the post-treatment steps described above may include processes that are common in steelmaking processes such as rolling processes. Additionally, method 100 further includes step 118. In step 118, when the result of the test in step 114 is negative, it is predicted that the continuous casting steel blank should have a surface transverse crack, so that the above-mentioned continuous casting steel blank is subjected to a remedial step. In a particular embodiment, the above remedial steps may include common measures such as inspection, grinding, and repair welding. Referring to Figure 3, there is shown a flow chart of a method for predicting whether a continuous casting steel blank has a surface transverse crack in accordance with another embodiment of the present invention. A method 300 of predicting whether a continuous casting steel blank has a surface transverse crack (referred to as "predictive method 300" for simplicity) is similar to the above-described prediction method 100, except for steps 304 and 306, Step 302 and step 308 to step 318 are respectively corresponding to step 102 and step 108 to step 118, so that the relevant change portion is not repeated, and only the difference step 304 and step 306 will be described below. In step 304, a tensile test is performed on the test piece of each historical continuous casting steel in step 302 to obtain a plurality of ductility indexes corresponding to the total amount of the plurality of first precipitates, wherein the plurality of first precipitations The total amount of objects corresponds to a plurality of ductility indicators in a one-to-one manner. Next, in step 306, based on the plurality of ductility indicators and the plurality of first precipitates corresponding to the ductility index, a threshold value of the total amount of precipitates corresponding to the plurality of ductility indicators is changed. . In addition, according to experimental data, the above-mentioned total precipitate critical value [s] 12 201233990 corresponds to the critical condition of whether or not a plurality of historical continuous casting steel blanks in step 302 generate surface lateral cracks. Further, the prediction method 100 has consistency with the threshold value of the total amount of precipitates obtained by the prediction method 300, respectively. In a particular embodiment, the specific component specifications in steps 102, 108, 302, and 308 of the above-described prediction methods 100 and 300 include a plurality of components in weight percent (wt%) as follows, wherein the components are: 0.07 to 0.17 wt% of carbon (C), 1.7 wt% or less of manganese (Μη), 0.02 wt% of phosphorus (P), 0.01 wt% or less of sulfur (S), and 0.2 to 1.0 wt%/〇 (Si), 0.01 to 0.05 wt% of aluminum (A1), 0.01 to 0.1 wt% of niobium (Nb), 0.01 to 0.1 wt% of vanadium (V), 0.030 wt% of titanium (Ti), 0.030 wt% The following boron (B), nitrogen (N) of 0.01 wt% or less, unavoidable impurities, and other parts (residues) composed of iron (Fe). In addition, in this embodiment, at least two of the above steps 102, 108, 302, and 308 may be aluminum nitride (A1N), niobium carbide (NbC), titanium nitride (TiN), vanadium carbide (VC). And any of the nitriding sheds (BN). The invention is more specifically described in the following examples, but the scope of the invention is not limited by the examples. Example for preparing steel for high-strength low-alloy structure First, the content of components of a plurality of historical molten steels is provided, wherein the content of each historical molten steel component falls within the range of specific component specifications listed below. . This specific composition specification includes the following components in wt%, and these components are: 0.07 to 0.17 wt% of carbon, 1.2 to 1.4 wt% of manganese, 0.02 wt% of phosphorus, and 0 to 008 wt% of sulfur. , 0.2~0.4 wt0/〇, 0.01~0.05 wt% aluminum, 0.01~0.03 wt% 铌, 0.008 重量% [s] 13 201233990 The following nitrogen, points. The unavoidable impurities and the other parts of the iron are dedicated to the content of the constituents of the above-mentioned plurality of historical steel liquids, and the content of each of the embryos contained in the embryos, the content of the pounds, and the precipitation The content of the substance is β I I, and should be the total number I of the first precipitates of the historical continuous casting steel. Its A, historical connection ^ η 运 运 "" steel embryo contains precipitates of antimony aluminum and tantalum carbide, so the above-mentioned "Gushan said 3, the total amount of precipitates is equal to gasification I Lu and broken sharp precipitation The sum of the quantities.
檢測每個歷史連鑄鋼胚，藉此獲得多個歷史連鑄鋼胚 ，應於上述多個第一析出物總量之多個表面橫向裂縫指 & ° f上述多個表面橫向裂縫指標分別對歷史鋼液之鋁與 氮t置i乘積、銳與碳含量之乘積、前述鋁氮含量乘積與 銳石反^量乘積之和 '以及氮化鋁及碳化鈮析出量之和做圖 (參見第4至7圖）。在鋁氮含量乘積與鈮碳含量乘積之和 中，因考慮四個元素之原子量差異，因此將鈮碳含量乘積 乘以一修正係數r之後，再與鋁氮含量乘積相加，其中修 正係數Γ稱為乘積當量，其計算方式如下： 修正係數r=(銘原子量X氮原子量)/(鈮原子量X碳原子 *)=(27χΐ4)/(93χΐ2)= 0.339 此外’氮化鋁及碳化鈮析出量之和係以原子百分比 (at%)為單仅。 接著，針對上述每個歷史連鑄鋼胚之試片，於750〜1200 °C進行拉伸試驗，藉此獲得對應於上述多個第一析出物總 量的多個延展性指標。此外’將上述多個延展性指標對氮 14 201233990 化鋁及碳化鈮析出量之和做圖（參見第8圖）。另外，在第8 圖中，可利用如最小平方法（Least Square)之曲線擬合 (Curve Fitting)方法求得虛線L，藉由虛線L來表示延展性 指標隨著氮化鋁及碳化鈮析出量之和變化之趨勢。 根據第7圖所示之内容，可歸納出對應於上述多個歷 史連鑄鋼胚不會產生表面橫向裂縫之析出物總量臨界值 0.04 at%，亦即氮化鋁及碳化鈮之析出量總和若小於〇〇4 at°/〇，則歷史連鑄鋼胚不會產生表面橫向裂縫。Detecting each historical continuous casting steel embryo, thereby obtaining a plurality of historical continuous casting steel embryos, respectively, a plurality of surface transverse crack fingers corresponding to the total amount of the plurality of first precipitates, and a plurality of surface lateral crack indexes respectively The sum of the product of aluminum and nitrogen t in the history of molten steel, the product of sharp and carbon content, the sum of the product of the above-mentioned aluminum nitrogen content and the product of the sharp stone, and the sum of the precipitation of aluminum nitride and tantalum carbide (see Figures 4 to 7). In the sum of the product of the aluminum nitrogen content and the enthalpy carbon content, considering the atomic weight difference of the four elements, the product of the 铌 carbon content is multiplied by a correction coefficient r, and then added to the product of the aluminum nitrogen content, wherein the correction coefficient Γ It is called the product equivalent and is calculated as follows: Correction coefficient r = (Ming atomic weight X nitrogen atomic weight) / (铌 atomic weight X carbon atom *) = (27χΐ4) / (93χΐ2) = 0.339 In addition, 'Aluminum nitride and niobium carbide precipitation The sum is based on the atomic percentage (at%). Next, a tensile test was conducted at 750 to 1200 °C for each test piece of each of the historical continuous cast steel blanks, thereby obtaining a plurality of ductility indexes corresponding to the total amount of the plurality of first precipitates. In addition, the above-mentioned plurality of ductility indexes are plotted against the sum of the precipitation of nitrogen and 2012 bismuth (see Fig. 8). In addition, in Fig. 8, the dotted line L can be obtained by a curve fitting method such as Least Square, and the ductility index can be expressed by aluminum nitride and tantalum carbide by a broken line L. The trend of the sum of the quantities. According to the content shown in Fig. 7, it can be concluded that the total amount of precipitates corresponding to the plurality of historical continuous casting steel blanks does not cause surface lateral cracks is 0.04 at%, that is, the precipitation amount of aluminum nitride and tantalum carbide. If the sum is less than 〇〇4 at ° / 〇, the historical continuous casting steel embryo will not produce surface transverse cracks.
然而，根據第4至6圖可知，無論使用鋁氮含量乘積、 銳碳含量乘積、或鋁氮含量乘積與鈮碳含量乘積之和，皆 無法明確歸納出表面橫向裂縫指標之變化趨勢。當第4至 6圖中之橫轴位在高乘積值之區域時，表面橫向裂縫指標 分布範圍介於0〜100%，亦即表示在相同乘積值下，部分批 次之產品並無表面橫向裂縫，但另一批次之產品幾乎全數 產生表面橫向裂缝，故表示組成元素之乘積無法有效預測 產品發生表面橫向裂縫的機率。反觀第7圖中氮化鋁及碳 化鈮析出量之和與表面橫向裂縫指標之間的關係，數據分 布相對較為收傲，可以明確界定出表面橫向裂縫發生斑否 的臨界值G.04 at%，故可更準確地預測產品是否發生㈣ —再者，根據第8圖所示之内容可知，當虛線[所㈣ 之虱化鋁及碳化鈮析出量之和超過〇 〇4at%(亦即點A所重 應之氮化減碳化㈣出量之和）時，歷史連軸胚試片j =性指標產生急㈣化(下降），此即表示歷史連铸細 域片之延展性迅速下降。而對照第7圖所示之内容可知 201233990 f氮化銘及碳⑽析0之和超過0.()4 at%之後，歷史連 之表面橫向裂縫指標開始升高(歷史連鑄鋼胚開始 碑…面橫向裂縫）’此印表示當歷史連鑄鋼胚之延展性指 二箱Ί時、對應之表面横向裂縫指標就越高’此即驗證上 :方法⑽與預剛方法綱分別獲得之析出物總量臨However, according to Figures 4 to 6, it can be seen that regardless of the product of the product of aluminum nitrogen content, the product of sharp carbon content, or the product of the product of aluminum and nitrogen content and the product of cerium carbon content, it is impossible to clearly summarize the trend of the surface lateral crack index. When the horizontal axis in Figures 4 to 6 is in the region of high product value, the surface lateral crack index distribution ranges from 0 to 100%, which means that under the same product value, some batches of products have no surface lateral direction. Cracks, but almost all of the products in the batch produce surface transverse cracks, so the product of the constituent elements cannot effectively predict the probability of surface lateral cracks in the product. In contrast, the relationship between the sum of precipitation of aluminum nitride and tantalum carbide and the surface lateral crack index in Figure 7 is relatively high, and the critical value of the surface transverse crack occurrence can be clearly defined. G.04 at% Therefore, it is possible to predict more accurately whether the product has occurred (4). Furthermore, according to the contents shown in Fig. 8, when the sum of the amount of deuterated aluminum and niobium carbide in the dotted line [(4) exceeds 〇〇4 at% (that is, the point) When A is reconciled to the nitriding and carbonization (fourth sum), the historical concentric test piece j = the sex indicator produces an urgent (four) (decrease), which means that the ductility of the historical continuous casting fine film is rapidly declining. According to the content shown in Figure 7, it can be seen that after the sum of 201233990 f nitriding and carbon (10) is more than 0. () 4 at%, the surface transverse crack index of the historical joint begins to rise (historical continuous casting steel embryo start monument) ...face lateral crack)' This mark indicates that when the ductility of the historical continuous casting steel is two boxes, the corresponding surface transverse crack index is higher. This is the verification: the method (10) and the pre-rigid method are respectively obtained. Total amount of material
ί = Γ致性的說法。此外，根據以上所述可知，點A 界狀、兄(象1上述歷史連缉鋼胚是否產生表面橫向裂縫之臨 界狀= 參見以上與步驟3〇6相關之說明）。 驗室分析即可評估出鋼H圖、之比較說明可知，可透過實 係，而不需透過大量生卜成刀與表面橫向裂縫指標之關 流程管制標準，可夫^式驗之品質評估結果來建立生產 了大㈣省試誤過程之成本。 此外，根據第7圖可知 技藝者可自行調整 ，在實際生產管理上’熟悉此 的管制值，而不以第氮化銘及碳化銳析出量之總和 at〇/〇為限。 所不之析出物總量臨界值〇.〇4 上述預測方法1〇〇及3〇〇 並儲存於一電腦 了實作為一電腦程式產品， 式產品並執::=錄媒體中，當電腦載入此電腦程 述電腦可讀取記錚測方法1〇0及300。其中，上 碟、硬碟、光碟為唯讀記憶體、快閃記憶體、軟 或熟悉此技藝者可二田、2、可由網路存取之資料庫 錄媒體。 I易心及具有相同功能之電腦可讀取紀 定本實施:式揭露如上，然其並非用以限 本發月任何热習此技藝者，在不脫離本發明之精神和 201233990 範圍内，當可作各種之更動與潤飾，因此本發明之保護範 . 圍當視後附之申請專利範圍所界定者為準。 【圖式簡單說明】 為了能夠對本發明之觀點有較佳之理解，請參照上述 之詳細說明並配合相應之圖式。要強調的是，根據工業之 標準常規，附圖中之各種特徵並未依比例繪示。事實上， 為清楚說明上述實施例，可任意地放大或縮小各種特徵之 0 尺寸。相關圖式内容說明如下。 第1圖係綠示根據本發明之一實施例之預測連鑄鋼胚 是否具有表面橫向裂縫的方法的流程圖。 第2A至2C圖係分別繪示在卜MC之析出反應 式中，不同析出階段之MC析出量與[M]/[C]比值的關係。 第3圖係繪示根據本發明之另一實施例之預測連鑄鋼 胚是否具有表面橫向裂縫的方法的流程圖。 第4至7圖係分別繪示根據本發明之一實施例之表面 • 橫向裂縫指標對歷史鋼液之鋁與氮含量之乘積、鈮與碳含 量之乘積、前述紹氮含量乘積與鈮碳含量乘積之和、以及 氮化鋁及碳化鈮析出量之和的關係。 第8圖係綠示第4至7圖之實施例之延展性指標對歷 史鋼液之氮化鋁及碳化鈮析出量之和的關係。 【主要元件符號說明】 100 :預，連_胚是否具有表面橫向裂縫的方法 1〇2·计算多個歷史連禱鋼胚中之多個第-析出物總量 m 201233990 104 :獲得多個表面橫向裂縫指標 • 106:歸納出對應於多個歷史連鑄鋼胚不會產生表面橫向裂 . 縫的析出物總量臨界值 108 .提供鋼液 110 :定量分析此鋼液之組成成分的含量 112 :計算連鑄鋼胚中之第二析出物總量 114 :比較第二析出物總量是否小於析出物總量臨界值，並 獲得檢驗結果 116 :對連鑄鋼胚進行後處理步驟 • 118 :對連鑄鋼胚進行補救步驟 300 :預測連鑄鋼胚是否具有表面橫向裂縫的方法 302 :計算多個歷史連鑄鋼胚中之多個第一析出物總量 304 :針對每個歷史連鑄鋼胚之試片進行拉伸試驗，藉此獲 得對應於多個第一析出物總量的多個延展性指標 306 :根據多個延展性指標及其對應的多個第一析出物總 量，歸納出對應於多個延展性指標產生急劇變化的析 出物總量臨界值，此臨界值對應於歷史連鑄鋼胚是否 • 產生表面橫向裂縫之臨界狀況 308 :提供鋼液 310 :定量分析此鋼液之組成成分的含量 312 :計算連鑄鋼胚中之第二析出物總量 314:比較第二析出物總量是否小於析出物總量臨界值，並 獲得檢驗結果 316 :對連鑄鋼胚進行後處理步驟 ' 318 :對連鑄鋼胚進行補救步驟 - [S] 18 201233990 A :點 [C]:固溶度 * [C]〇 :起始固溶度 L :虛線 . [M]:固溶度 [M]〇 :起始固溶度 I S1ί = a statement of coherence. Further, as can be seen from the above, the point A boundary shape, the brother (like the above-mentioned historical tantalum steel embryo whether or not the surface lateral crack is bordered = see the description related to step 3〇6 above). The laboratory analysis can evaluate the steel H-graph, and the comparison description shows that the quality can be passed through the real system without the need to pass through a large number of raw knives and surface lateral crack indicators. To establish the cost of producing a large (four) provincial trial and error process. In addition, according to Fig. 7, the skilled person can adjust it himself and be familiar with the control value of the actual production management, and not limited to the sum of the nitriding and carbonization precipitation at〇/〇. The total value of the total amount of precipitates is 〇.〇4 The above prediction methods are 1〇〇 and 3〇〇 and are stored in a computer as a computer program product, and the product is executed: := recorded media, when the computer contains Into this computer program computer can read the recording method 1 〇 0 and 300. Among them, the upper disc, hard disc, and optical disc are read-only memory, flash memory, soft, or those skilled in the art, and can access the media in the database. I am embarrassed and have the same function of the computer can read the implementation of this document: the above disclosure, but it is not intended to limit the experience of any person in this month, without departing from the spirit of the present invention and 201233990, when Various modifications and refinements are made, and thus the scope of protection of the present invention is defined by the scope of the patent application. BRIEF DESCRIPTION OF THE DRAWINGS In order to provide a better understanding of the present invention, reference is made to the above detailed description and the accompanying drawings. It is emphasized that the various features in the drawings are not drawn to scale in accordance with the standard of the industry. In fact, to clearly illustrate the above embodiments, the 0 dimensions of the various features can be arbitrarily enlarged or reduced. The relevant schema description is as follows. BRIEF DESCRIPTION OF THE DRAWINGS Figure 1 is a flow chart showing a method of predicting whether a continuous casting steel blank has a surface transverse crack according to an embodiment of the present invention. The 2A to 2C graphs respectively show the relationship between the amount of MC precipitated at different precipitation stages and the ratio of [M]/[C] in the precipitation reaction formula of the MC. Figure 3 is a flow chart showing a method of predicting whether a continuous casting steel has a surface transverse crack in accordance with another embodiment of the present invention. 4 to 7 are respectively a product of the surface and transverse crack index according to an embodiment of the present invention, the product of the aluminum and nitrogen content of the historical molten steel, the product of the cerium and the carbon content, the product of the above-mentioned nitrogen content, and the carbon content of the cerium. The sum of the products and the relationship between the sum of the precipitation of aluminum nitride and tantalum carbide. Fig. 8 is a graph showing the relationship between the ductility index of the examples of Figs. 4 to 7 and the sum of the precipitation amounts of aluminum nitride and niobium carbide in the history steel liquid. [Explanation of main component symbols] 100: Pre-, _ embryo whether there is a surface lateral crack method 1 〇 2 · Calculate the total number of multiple - precipitates in multiple historical prayer embryos 201233990 104 : Obtain multiple surfaces Transverse crack index • 106: Inductively corresponds to multiple historical continuous casting steel embryos without surface lateral cracking. Sediment total sediment critical value 108. Provide molten steel 110: Quantitative analysis of the content of this molten steel component 112 : Calculating the total amount of the second precipitate in the continuous casting steel 114: comparing whether the total amount of the second precipitate is smaller than the critical value of the total amount of the precipitate, and obtaining the test result 116: post-processing step for the continuous casting steel embryo • 118: Remediation step 300 for continuous casting steel blanks: Method for predicting whether a continuous casting steel ore has a surface transverse crack 302: Calculating a total of a plurality of first precipitates in a plurality of historical continuous casting steel blanks 304: for each historical continuous casting The test piece of the steel blank is subjected to a tensile test, thereby obtaining a plurality of ductility indexes 306 corresponding to the total amount of the plurality of first precipitates: according to the plurality of ductility indicators and the corresponding plurality of first precipitates, Inductively corresponding to multiple delays The indicator produces a sharply varying critical value of the total amount of precipitates, which corresponds to the history of the continuous casting of the steel. • The critical condition of the surface transverse crack is generated 308: Supply of molten steel 310: Quantitative analysis of the composition of the molten steel 312 : Calculating the total amount of the second precipitate in the continuous casting steel 314: comparing whether the total amount of the second precipitate is smaller than the critical value of the total amount of the precipitate, and obtaining the test result 316: performing the post-processing step on the continuous casting steel embryo 318 : Remediation step for continuous casting steel - [S] 18 201233990 A : Point [C]: Solid solubility * [C] 〇: Initial solid solubility L: dotted line. [M]: Solid solubility [M] 〇 : Initial solid solubility I S1
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