TWI404806B - High strength non - directional electrical steel sheet and its manufacturing method - Google Patents
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Abstract
Description
本發明係有關適合於電動汽車用馬達與電動機器用馬達的鐵芯材料之高強度無方向性電磁鋼板及其製造方法。The present invention relates to a high-strength non-oriented electrical steel sheet suitable for a core material of a motor for an electric vehicle and a motor for an electric motor, and a method of manufacturing the same.
近年來，由於世界性的電動機器之節能意識高漲，對於用為旋轉機的鐵芯材料之無方向性電磁鋼板，要求具有較高性能之特性。最近，特別是作為用於電動汽車等之馬達，高度需求小型且高輸出之馬達。該類之電動汽車用馬達，被設計成可高速旋轉以得到高轉矩。In recent years, due to the high energy-saving awareness of the worldwide electric machine, the non-oriented electrical steel sheet used as the core material of the rotating machine is required to have high performance characteristics. Recently, particularly as a motor for an electric vehicle or the like, a motor that is small in size and high in output is highly demanded. Motors for electric vehicles of this type are designed to be rotated at a high speed to obtain high torque.
高速旋轉馬達，亦被用在工作機械及吸塵機等電動機器。但是，電動汽車用的高速旋轉馬達之外形，大於電動機器用的高速旋轉馬達之外形。又，作為電動汽車用的高速旋轉馬達，以使用直流無刷馬達為主。直流無刷馬達中，有磁石填補於轉子之外周附近。該構造中，轉子之外周部的橋部之寬度(從轉子之最外周至磁石間之鋼板的寬度)，隨著部位約為1~2毫米且非常狹。因此，電動汽車用的高速旋轉馬達中，被要求由傳統的無方向性電磁鋼板轉用高強度之鋼板。High-speed rotary motors are also used in electric machines such as work machines and vacuum cleaners. However, the shape of the high-speed rotary motor for electric vehicles is larger than that of the high-speed rotary motor for electric machines. Further, as a high-speed rotary motor for an electric vehicle, a DC brushless motor is mainly used. In the DC brushless motor, a magnet is filled in the vicinity of the outer circumference of the rotor. In this configuration, the width of the bridge portion at the outer peripheral portion of the rotor (from the outermost circumference of the rotor to the width of the steel plate between the magnets) is very narrow as the portion is about 1 to 2 mm. Therefore, in a high-speed rotary motor for an electric vehicle, it is required to switch from a conventional non-oriented electromagnetic steel sheet to a high-strength steel sheet.
專利文獻1中，已記載Si中添加Mn及Ti，以求得固熔體強化之無方向性電磁鋼板。但是，雖依賴該無方向性電磁鋼板，亦無法得到充分之強度。又，隨著未添加Mn及Ti，易於降低韌性，充分之生產性及成品率無法獲得。又，被添加的合金之價格高昂。近年來，特別是由於世界性之供需平衡，鈦之價格高漲。Patent Document 1 describes a non-oriented electrical steel sheet in which Mn and Ti are added to Si to obtain solid solution strengthening. However, depending on the non-oriented electrical steel sheet, sufficient strength cannot be obtained. Further, with the addition of Mn and Ti, it is easy to reduce the toughness, and sufficient productivity and yield cannot be obtained. Also, the price of the alloy to be added is high. In recent years, especially due to the balance of supply and demand in the world, the price of titanium has risen.
專利文獻2及3中，已記載分散碳氮化物於鋼中以謀求強化之無方向性電磁鋼板。但是，雖依賴該等之無方向性電磁鋼板，亦無法得到充分之強度。In Patent Documents 2 and 3, a non-oriented electrical steel sheet in which a carbonitride is dispersed in steel to be strengthened is described. However, sufficient strength cannot be obtained by relying on such non-oriented electrical steel sheets.
專利文獻4中，已記載使用Cu析出物以謀求強化之無方向性電磁鋼板。但是，製造該無方向性電磁鋼板時，受限於熱處理條件。因此，無法得到所要求之強度及磁性特性。Patent Document 4 describes a non-oriented electrical steel sheet in which Cu precipitates are used for reinforcement. However, when the non-oriented electrical steel sheet is produced, it is limited by the heat treatment conditions. Therefore, the required strength and magnetic properties cannot be obtained.
【專利文獻1】特開昭62-256917號公報[Patent Document 1] JP-A-62-256917
【專利文獻2】特開平06-330255號公報[Patent Document 2] Japanese Patent Publication No. 06-330255
【專利文獻3】特開平10-018005號公報[Patent Document 3] Japanese Patent Laid-Open No. Hei 10-018005
【專利文獻4】特開2004-084053號公報[Patent Document 4] JP-A-2004-084053
本發明之目的在於提供易於得到具有高強度與磁性特性之高強度無方向性電磁鋼板及其製造方法。An object of the present invention is to provide a high-strength non-oriented electrical steel sheet which is easy to obtain high strength and magnetic properties and a method for producing the same.
本發明為解決前述課題，以下為其要旨。The present invention has been made in order to solve the above problems.
(I)一種高強度無方向性電磁鋼板，其特徵在於：以質量%計，含有：C：0.002%以上、0.05%以下；Si：2.0%以上、4.0%以下；Mn：0.05%以上、1.0%以下；N：0.002%以上、0.05%以下；及Cu：0.5%以上、3.0%以下；且Al之含量為3.0%以下；並且令Nb之含量(%)為[Nb]、Zr之含量(%)為[Zr]、Ti之含量(%)為[Ti]、V之含量(%)為[V]、C之含量(%)為[C]、N之含量(%)為[N]時，滿足通式(1)及通式(2)；殘餘部分係由Fe及不可避免之不純物構成；再結晶面積率為50%以上；拉伸試驗之降伏應力為700MPa以上；破斷伸長率為10%以上；渦流損失We10/400 (W/kg)與鋼板之板厚t(mm)的關係中，滿足通式(3)。(I) A high-strength non-oriented electrical steel sheet comprising, by mass%, C: 0.002% or more and 0.05% or less; Si: 2.0% or more and 4.0% or less; Mn: 0.05% or more, 1.0. % or less; N: 0.002% or more and 0.05% or less; and Cu: 0.5% or more and 3.0% or less; and the content of Al is 3.0% or less; and the content (%) of Nb is the content of [Nb] and Zr ( %) is [Zr], Ti content (%) is [Ti], V content (%) is [V], C content (%) is [C], and N content (%) is [N] When the general formula (1) and the general formula (2) are satisfied; the residual portion is composed of Fe and unavoidable impurities; the recrystallization area ratio is 50% or more; the tensile stress of the tensile test is 700 MPa or more; the elongation at break It is 10% or more; the relationship between the eddy current loss We 10/400 (W/kg) and the sheet thickness t (mm) of the steel sheet satisfies the general formula (3).
2.0×10-4 ≦[Nb]/93＋[Zr]/91＋[Ti]/48＋[V]/51……(1)2.0×10 -4 ≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51......(1)
1.0×10-3 ≦[C]/12＋[N]/14-([Nb]/93＋[Zr]/91＋[Ti]/48＋[V]/51)≦3.0×10-3 ……(2)1.0×10 -3 ≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10 -3 ......(2)
We10/400 ≦70×t2 ……(3)We 10/400 ≦70×t 2 ......(3)
(II)第(I)項記載之高強度無方向性電磁鋼板，以質量%計，其中更含有Ni：0.5%以上、3.0%以下。(II) The high-strength non-oriented electrical steel sheet according to the item (I), which further contains, by mass%, Ni: 0.5% or more and 3.0% or less.
(III)第(I)或(II)項記載之高強度無方向性電磁鋼板，以質量%計，其中更含有Sn：0.01%以上、0.10%以下。(III) The high-strength non-oriented electrical steel sheet according to the item (I) or (II), which further contains, by mass%, 0.01% or more and 0.10% or less.
(IV)第(I)至(III)項中任一項記載之高強度無方向性電磁鋼板，以質量%計，其中更含有B：0.0010%以上、0.0050%以下。(IV) The high-strength non-oriented electrical steel sheet according to any one of the items (1) to (III), further comprising, by mass%, B: 0.0010% or more and 0.0050% or less.
(V)一種高強度無方向性電磁鋼板之製造方法，其特徵在於具有以下步驟：(V) A method of manufacturing a high-strength non-oriented electrical steel sheet, comprising the steps of:
製作平板之步驟，且該平板以質量%計，含有：C：0.002%以上、0.05%以下；Si：2.0%以上、4.0%以下；Mn：0.05%以上、1.0%以下；N：0.002%以上、0.05%以下；及Cu：0.5%以上、3.0%以下；且Al之含量為3.0%以下；並且令Nb之含量(%)為[Nb]、Zr之含量(%)為[Zr]、Ti之含量(%)為[Ti]、V之含量(%)為[V]、C之含量(%)為[C]、N之含量(%)為[N]時，滿足通式(1)及通式(2)；又，殘餘部分為Fe及不可避免之不純物所構成；進行前述鋼之熱軋，以得到熱軋板之步驟；進行前述熱軋板之酸洗之步驟；其次，進行前述熱軋板之冷軋，以得到冷軋板之步驟；及進行前述冷軋板之精加工退火之步驟；且前述精加工退火之均熱溫度T(℃)與前述冷軋板之Cu含量a(質量%)滿足通式(4)。a step of producing a flat plate containing, in mass%, C: 0.002% or more and 0.05% or less; Si: 2.0% or more and 4.0% or less; Mn: 0.05% or more and 1.0% or less; and N: 0.002% or more , 0.05% or less; and Cu: 0.5% or more and 3.0% or less; and the content of Al is 3.0% or less; and the content (%) of Nb is [Nb], and the content (%) of Zr is [Zr], Ti When the content (%) is [Ti], the content (%) of V is [V], the content (%) of C is [C], and the content (%) of N is [N], the formula (1) is satisfied. And the general formula (2); further, the residual portion is composed of Fe and unavoidable impurities; the step of performing hot rolling of the steel to obtain a hot rolled sheet; performing the pickling step of the hot rolled sheet; secondly, performing Cold rolling of the hot-rolled sheet to obtain a cold-rolled sheet; and a step of finishing annealing of the cold-rolled sheet; and a soaking temperature T (°C) of the finishing annealing and a Cu content of the cold-rolled sheet a (% by mass) satisfies the formula (4).
T≧200×a＋500……(4)T≧200×a+500......(4)
(VI)第(V)項記載之高強度無方向性電磁鋼板之製造方法，其中在得到前述熱軋板之步驟與進行前述酸洗之步驟間，具有進行前述熱軋板之退火之步驟。(VI) The method for producing a high-strength non-oriented electrical steel sheet according to the item (V), wherein the step of obtaining the hot-rolled sheet and the step of performing the pickling have a step of annealing the hot-rolled sheet.
(VII)一種高強度無方向性電磁鋼板之製造方法，其特徵在於具有以下步驟：(VII) A method for producing a high-strength non-oriented electrical steel sheet, comprising the steps of:
製作平板之步驟，且該平板以質量%計，含有：a step of making a flat plate, and the flat plate is in mass %, and contains:
C：0.002%以上、0.05%以下；C: 0.002% or more and 0.05% or less;
Si：2.0%以上、4.0%以下；Si: 2.0% or more and 4.0% or less;
Mn：0.05%以上、1.0%以下；Mn: 0.05% or more and 1.0% or less;
N：0.002%以上、0.05%以下；及N: 0.002% or more and 0.05% or less; and
Cu：0.5%以上、3.0%以下；且Cu: 0.5% or more and 3.0% or less;
Al之含量為3.0%以下；並且當令Nb之含量(%)為[Nb]、Zr之含量(%)為[Zr]、Ti之含量(%)為[Ti]、V之含量(%)為[V]、C之含量(%)為[C]、N之含量(%)為[N]時，滿足通式(1)及通式(2)；又，殘餘部分由Fe及不可避免之不純物所構成；進行前述鋼之熱軋，以得到熱軋板之步驟；其次，進行前述熱軋板之酸洗之步驟；其次，進行前述熱軋板之冷軋，以得到冷軋鋼之步驟；及進行前述冷軋板之精加工退火之步驟；又，前述熱軋之捲取溫度為500℃以下，且前述熱軋板之夏丕氏衝擊試驗中之延性脆性斷面轉移溫度為70℃以下。The content of Al is 3.0% or less; and when the content (%) of Nb is [Nb], the content (%) of Zr is [Zr], the content (%) of Ti is [Ti], and the content (%) of V is When the content (%) of [V] and C is [C], and the content (%) of N is [N], the general formula (1) and the general formula (2) are satisfied; and the residual portion is Fe and inevitable. a step of forming a hot-rolled sheet by hot rolling of the steel; a step of pickling the hot-rolled sheet; and a step of cold-rolling the hot-rolled sheet to obtain a cold-rolled steel; And performing the step of finishing annealing of the cold-rolled sheet; further, the coiling temperature of the hot rolling is 500 ° C or less, and the ductile brittle section transition temperature in the Charpy impact test of the hot-rolled sheet is 70 ° C or less .
2.0×10-4 ≦[Nb]/93＋[Zr]/91＋[Ti]/482.0×10 -4 ≦[Nb]/93+[Zr]/91+[Ti]/48
(VIII)一種高強度無方向性電磁鋼板之製造方法，其特徵在於具有以下步驟：製作平板之步驟，且該平板以質量%計，含有：C：0.002%以上、0.05%以下；Si：2.0%以上、4.0%以下；Mn：0.05%以上、1.0%以下；N：0.002%以上、0.05%以下；及Cu：0.5%以上、3.0%以下；且Al之含量為3.0%以下；並且當令之Nb之含量(%)為[Nb]、Zr之含量(%)為[Zr]、Ti之含量(%)為[Ti]、V之含量(%)為[V]、C之含量(%)為[C]、N之含量(%)為[N]時，滿足通式(1)及通式(2)；又，殘餘部分由Fe及不可避免之不純物所構成；進行前述鋼之熱軋，以得到熱軋板之步驟；其次，進行前述熱軋板之退火之步驟；其次，進行熱軋板之酸洗之步驟；其次，進行前述熱軋板之冷軋，以得到冷軋板之步驟；及進行前述冷軋板之精加工退火之步驟；又，前述退火從900℃至500℃之冷卻速度為50℃/sec以上，且前述熱軋板之夏丕氏衝擊試驗中之延性脆性斷面轉移溫度為70℃以下。(VIII) A method for producing a high-strength non-oriented electrical steel sheet, comprising the steps of: forming a flat plate, wherein the flat plate contains, by mass%, C: 0.002% or more and 0.05% or less; Si: 2.0 % or more, 4.0% or less; Mn: 0.05% or more and 1.0% or less; N: 0.002% or more and 0.05% or less; and Cu: 0.5% or more and 3.0% or less; and Al content of 3.0% or less; The content (%) of Nb is [Nb], the content (%) of Zr is [Zr], the content (%) of Ti is [Ti], the content (%) of V is [V], and the content of C (%) When the content (%) of [C] and N is [N], the general formula (1) and the general formula (2) are satisfied; and the residual portion is composed of Fe and unavoidable impurities; the hot rolling of the aforementioned steel is performed. a step of obtaining a hot rolled sheet; secondly, performing the step of annealing the hot rolled sheet; secondly, performing a pickling step of the hot rolled sheet; and secondly, performing cold rolling of the hot rolled sheet to obtain a cold rolled sheet a step of finishing annealing of the cold-rolled sheet; and a cooling rate of the annealing from 900 ° C to 500 ° C of 50 ° C / sec or more, and the Charpy impact test of the hot-rolled sheet The ductile brittle section transition temperature is below 70 °C.
本發明人等，有關活用Cu析出物之一般的鋼強化方法，對於熱處理條件大幅度影響到強度及磁性特性之理由進行調查。其結果，發現為要以Cu的析出物強化鋼板，須在冷軋後之精加工退火時，有必要使Cu一旦固熔之高退火溫度。The inventors of the present invention investigated the reason why the heat treatment conditions greatly affect the strength and magnetic properties in the general steel strengthening method in which Cu precipitates are used. As a result, it was found that in order to strengthen the steel sheet with precipitates of Cu, it is necessary to make the Cu high solid annealing temperature once the finish annealing is performed after cold rolling.
但是，亦認知僅提高精加工退火溫度，使結晶粒粗大化，藉由Cu析出之強化損耗。However, it is also recognized that only the finishing annealing temperature is increased, the crystal grains are coarsened, and the strengthening loss by Cu precipitation is obtained.
再者，亦認知結晶粒之粗大化及Cu之析出強化重叠，則拉伸試驗中之破斷伸長率顯著地降低。該破斷伸長率之顯著地降低，特別於從鋼板鑿穿馬達芯時，在鑿穿面產生龜裂，發展成馬達芯之成品率及生產性顯著地降低。因此，期望避免破斷伸長率之顯著地降低。Further, it is also recognized that the coarsening of the crystal grains and the precipitation strengthening of the Cu overlap, the elongation at break in the tensile test is remarkably lowered. This breaking elongation is remarkably lowered, and in particular, when the motor core is cut from the steel sheet, cracks are generated at the piercing surface, and the yield and productivity of the motor core are remarkably lowered. Therefore, it is desirable to avoid a significant decrease in elongation at break.
因此，本發明人等發揮Cu之析出強化之同時，對於解決該等諸問題之方法，更認真進行研究。其結果，認知藉由含有某規定量之C、N、Nb、Zr、Ti及V，可使Cu之析出強化及結晶粒之微細化同時成立，可解決前述之諸問題。Therefore, the inventors of the present invention have conducted research on solving the problems of these problems while exerting the precipitation strengthening of Cu. As a result, it is recognized that the precipitation of the Cu and the refinement of the crystal grains can be simultaneously established by containing a certain amount of C, N, Nb, Zr, Ti, and V, and the above problems can be solved.
再者，認知高強度電磁鋼板的主要用途之轉子所要求的磁性特性，係400Hz或高於前者之高周波中的渦流損失(We)，雖於其減低之情形下，藉由含有之C、N、Nb、Zr、Ti及V之結晶粒微細化亦有效。Furthermore, the magnetic properties required for the rotor of the main purpose of the high-strength electromagnetic steel sheet are 400 Hz or higher than the eddy current loss (We) in the high frequency of the former, and in the case of the reduction, by containing C, N The grain refinement of Nb, Zr, Ti and V is also effective.
在此，說明有關完成本發明之試驗結果。Here, the test results relating to the completion of the present invention will be explained.
在試驗室之真空熔解爐中，以質量%計，製造含有Si：3.1%、Mn：0.2%、Al：0.5%、Cu：2.0%，及以第1表顯示的C、N、Nb、Zr、Ti及V之質量%之鋼，在1100℃加熱60分鐘後，立即熱軋，得到板厚為2.0毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中，得到板厚為0.35毫米之冷軋板。對於該冷軋板，在800℃~1000℃、實施30秒鐘之精加工退火。第2表中顯示精加工退火後之諸特性的測定結果。In the vacuum melting furnace of the laboratory, Si: 3.1%, Mn: 0.2%, Al: 0.5%, Cu: 2.0%, and C, N, Nb, Zr shown in Table 1 were produced by mass%. The steel of the mass% of Ti and V was hot-rolled immediately after heating at 1,100 ° C for 60 minutes to obtain a hot rolled sheet having a thickness of 2.0 mm. Then, the hot rolled sheet was subjected to pickling, and in one cold rolling, a cold rolled sheet having a thickness of 0.35 mm was obtained. The cold-rolled sheet was subjected to finishing annealing at 800 ° C to 1000 ° C for 30 seconds. The measurement results of the properties after finishing annealing are shown in Table 2.
如第2表所示，在Nb、Zr、Ti及V滿足通式(1)之原料C及D中，得到降伏強度及破斷伸長率高，且渦流損失低之優良特性。關於幾乎不含C、N、Nb、Zr、Ti及V之原料A，降伏強度及破斷伸長率皆低，渦流損失高。其在900℃及1000℃之精加工退火中，由於結晶粒之粗大化。As shown in the second table, in the raw materials C and D in which Nb, Zr, Ti, and V satisfy the general formula (1), excellent characteristics such as high lodging strength and elongation at break and low eddy current loss are obtained. Regarding the raw material A containing almost no C, N, Nb, Zr, Ti, and V, the lodging strength and the elongation at break were both low, and the eddy current loss was high. In the finishing annealing at 900 ° C and 1000 ° C, the crystal grains are coarsened.
關於原料B中，在900℃的精加工退火中之再結晶率低。據推想其由於微量含有之Nb，在於將進行精加工退火的再結晶之前析出，使再結晶遲延。又，據推想係發現由於1000℃之精加工退火中，使Nb固熔，結晶粒粗大化，與原料A之結果相同。Regarding the raw material B, the recrystallization ratio in the finishing annealing at 900 ° C was low. It is thought that since Nb is contained in a small amount, it is precipitated before recrystallization of the finish annealing, and the recrystallization is delayed. Further, it has been found that it is found that Nb is solid-melted in the finishing annealing at 1000 ° C, and the crystal grains are coarsened, which is the same as the result of the raw material A.
關於得到優良特性之原料C，Nb析出物適度地分散析出，關於原料D，據推想係Ti析出物適度地分散析出，在900℃及1000℃之結晶粒成長受到抑制。另一方面，Cu於900℃及1000℃之精加工退火中一旦固熔，更於精加工退火之冷卻時，由於微細地析出，故可活用Cu之析出強化至最大限度。其結果，據推想可得到高度之降伏強度及破斷伸長率，及低度之渦流損失。In the raw material C in which the excellent properties are obtained, the Nb precipitates are appropriately dispersed and precipitated, and it is estimated that the Ti precipitates are appropriately dispersed and precipitated in the raw material D, and the crystal grain growth at 900 ° C and 1000 ° C is suppressed. On the other hand, when Cu is solid-melted in the finishing annealing at 900 ° C and 1000 ° C, it is finely precipitated during cooling by finish annealing, so that the precipitation strengthening of Cu can be utilized to the maximum. As a result, it is estimated that a high drop strength and a breaking elongation, and a low eddy current loss can be obtained.
關於原料E係降伏強度高，但破斷伸長率低者。認為其受到過量的C之不良影響。又，在任何之條件中，在800℃之精加工退火中，未見再結晶。其認為係由於退火前固熔之Cu於退火中析出，使再結晶遲延。Regarding the raw material E, the drop strength is high, but the elongation at break is low. It is considered to be adversely affected by excessive C. Further, in any of the conditions, no recrystallization was observed in the finishing annealing at 800 °C. It is considered that the precipitation of Cu which is solidified before annealing is precipitated in the annealing, and the recrystallization is delayed.
在試驗室之真空熔解爐中，以質量%計，製造含有Si：2.8%、Mn：0.1%、Al：1.0%、Cu：1.8%，及以第3表顯示之C、N、Nb、Zr、Ti及V之質量%之鋼，在1150℃加熱60分鐘後，立即熱軋，得到板厚為2.2毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中，得到板厚為0.35毫米之冷軋板。對於該冷軋板，在800℃~1000℃實施30秒鐘之精加工退火。第4表中係顯示精加工退火後之諸特性的測定結果。In the vacuum melting furnace of the laboratory, Si: 2.8%, Mn: 0.1%, Al: 1.0%, Cu: 1.8%, and C, N, Nb, Zr shown in Table 3 were produced by mass%. The steel of the mass% of Ti and V was hot-rolled immediately after heating at 1,150 ° C for 60 minutes to obtain a hot-rolled sheet having a thickness of 2.2 mm. Then, the hot rolled sheet was subjected to pickling, and in one cold rolling, a cold rolled sheet having a thickness of 0.35 mm was obtained. For the cold-rolled sheet, finishing annealing was performed at 800 ° C to 1000 ° C for 30 seconds. In the fourth table, the measurement results of the properties after finishing annealing are shown.
如第4表所示，在Nb、Zr、Ti及V滿足通式(1)之原料H及I中，得到降伏強度及破斷伸長率高，且渦流損失低之優良特性。關於幾乎不含C、N、Nb、Zr、Ti及V之原料F，降伏強度及破斷伸長率皆低，渦流損失高。其在900℃及1000℃之精加工退火中，由於結晶粒之粗大化。As shown in the fourth table, in the raw materials H and I in which Nb, Zr, Ti, and V satisfy the general formula (1), excellent characteristics such as high lodging strength and elongation at break and low eddy current loss are obtained. Regarding the raw material F containing almost no C, N, Nb, Zr, Ti, and V, the fall strength and the elongation at break are both low, and the eddy current loss is high. In the finishing annealing at 900 ° C and 1000 ° C, the crystal grains are coarsened.
關於原料G中，在900℃之精加工退火中，再結晶率低。據推想其由於微量含有之Nb，在於將進行精加工退火的再結晶之前析出，使再結晶遲延。又，據推想係發現在1000℃之精加工退火中，Nb固熔，使結晶粒粗大化，與原料F之結果相同。Regarding the raw material G, the recrystallization ratio was low in the finishing annealing at 900 °C. It is thought that since Nb is contained in a small amount, it is precipitated before recrystallization of the finish annealing, and the recrystallization is delayed. Further, it has been found that in the finishing annealing at 1000 ° C, Nb is solid-melted to coarsen the crystal grains, which is the same as the result of the raw material F.
關於得到優良特性之原料H，Nb析出物適度地分散析出，關於原料I，據推想係Ti析出物適度地分散析出，在900℃及1000℃之結晶粒成長受到抑制。另一方面，Cu於900℃及1000℃之精加工退火中一旦固熔，更於精加工退火之冷卻時，由於微細地析出，故可活用Cu之析出強化至最大限度。其結果，據推想可得到高度之降伏強度及破斷伸長率，及低度之渦流損失。In the raw material H, which is excellent in characteristics, Nb precipitates are appropriately dispersed and precipitated. It is estimated that the Ti precipitates are appropriately dispersed and precipitated in the raw material I, and the crystal grain growth at 900 ° C and 1000 ° C is suppressed. On the other hand, when Cu is solid-melted in the finishing annealing at 900 ° C and 1000 ° C, it is finely precipitated during cooling by finish annealing, so that the precipitation strengthening of Cu can be utilized to the maximum. As a result, it is estimated that a high drop strength and a breaking elongation, and a low eddy current loss can be obtained.
關於原料J係降伏強度高，但破斷伸長率低者。認為其受到過量的C之不良影響。又，在任何之條件中，於800℃之精加工退火中未發現再結晶。其認為係在退火前固熔之Cu於退火中析出，使再結晶遲延。Regarding the raw material J, the drop strength is high, but the elongation at break is low. It is considered to be adversely affected by excessive C. Further, in any of the conditions, no recrystallization was observed in the finishing annealing at 800 °C. It is considered that Cu which is solid-melted before annealing is precipitated in the annealing to delay the recrystallization.
目前為止，在800℃之精加工退火係作為結晶粒之微細化處理實施。即，藉由該精加工退火，使Cu一旦固熔以求得高強度化，且使鋼板再結晶之外，在避免結晶粒粗大化為目的下進行。但是從試驗1及2，了解雖添加Cu之同時，調整退火溫度，僅進行該步驟，難於得到充分之強度。即以傳統之技術，難於使機械特性及磁性特性兩立。對此，根據以下所述之本發明，可使機械特性及磁性特性兩立。Finishing annealing at 800 °C has been carried out as a refining treatment of crystal grains. In other words, by the finish annealing, Cu is solid-melted to obtain high strength, and the steel sheet is recrystallized, and the crystal grains are coarsened. However, from Tests 1 and 2, it is understood that while Cu is added, the annealing temperature is adjusted, and only this step is performed, and it is difficult to obtain sufficient strength. That is, it is difficult to make both mechanical and magnetic properties stand by conventional techniques. On the other hand, according to the invention described below, both mechanical properties and magnetic properties can be achieved.
其次，敘述有關本發明相關之高強度無方向電磁鋼板中之數值的限定理由，以下，%係質量%之意。Next, the reason for limiting the numerical value in the high-strength non-oriented electrical steel sheet according to the present invention will be described. Hereinafter, % is the meaning of mass%.
C係結晶粒微細化上必要之元素。微細之碳化物，係增加再結晶時之核生成部位，更具有抑制結晶粒成長之效果。為發揮該效果，含C量為0.002%以上。特別是N小於0.005%時，C含量以0.01%以上為佳，較佳為0.02%以上。另一方面，添加大於0.05%，則破斷伸長率顯著地降低。因此，C含量之上限為0.05%。The elements necessary for the refinement of the crystal grains of the C system. The fine carbides increase the nucleation sites at the time of recrystallization and have an effect of suppressing the growth of crystal grains. In order to exert this effect, the C content is 0.002% or more. In particular, when N is less than 0.005%, the C content is preferably 0.01% or more, and more preferably 0.02% or more. On the other hand, when the addition is more than 0.05%, the elongation at break is remarkably lowered. Therefore, the upper limit of the C content is 0.05%.
Si係有效於減低渦流損失，同時亦是有效於固熔體強化之元素。但過度添加，則冷軋性顯著地降低。因此，Si之含量之上限為4.0%。另一方面，從固熔體強化及渦流損失之觀點言，下限為2.0%。The Si system is effective in reducing eddy current loss and is also an element effective for solid solution strengthening. However, if it is excessively added, the cold rolling property is remarkably lowered. Therefore, the upper limit of the content of Si is 4.0%. On the other hand, from the viewpoint of solid solution strengthening and eddy current loss, the lower limit is 2.0%.
Mn係與Si相同有效於降低渦流損失及提高強度之元素。但是Mn之含量雖大於1.0%，由於效果未見提高而飽和，故Mn之含量之上限為1.0%。另一方面，從硫化合物生成之觀點言，下限為0.05%。The Mn system is as effective as Si in reducing the eddy current loss and improving the strength. However, although the content of Mn is more than 1.0%, since the effect is not improved and saturated, the upper limit of the content of Mn is 1.0%. On the other hand, from the viewpoint of sulfur compound formation, the lower limit is 0.05%.
Al係與Si同樣地有效於增加電阻率之元素。但Al含量大於3.0%，由於鑄造性降低，考慮到生產性，故Al含量之上限為3.0%。關於下限，未特予規定。但是，從脫氧之穩定化(防止鑄造中之噴嘴阻塞)觀點言，鋁脫氧時之Al含量以 0.02%以上，Si脫氧時之含鋁量以0.01%以上為佳。The Al system is effective for increasing the resistivity element similarly to Si. However, the Al content is more than 3.0%, and since the castability is lowered, the upper limit of the Al content is 3.0% in view of productivity. Regarding the lower limit, no specific provisions are made. However, from the viewpoint of stabilizing deoxidation (preventing nozzle blockage during casting), the Al content during deoxidation of aluminum is More than 0.02%, the aluminum content in the case of deoxidation of Si is preferably 0.01% or more.
N係結晶粒微細化上必要之元素。微細的氮化物係增加再結晶時核生成部位，更具有抑制結晶粒成長之效果。為發揮該效果，N之含量為0.002%以上。如使N含有大幅度地大於一般水準之0.005%以上，則抑制結晶粒成長之效果更為顯著。該效果由於隨著N之含量愈高愈大，故更將N之含量增加至0.01%以上為佳，較佳為0.02%以上。特別是含C量小於0.005%時，藉由此類N之添加所得之效果顯示更為強烈。另一方面，大於0.05%添加，則破斷伸長率顯著地降低。因此，N之含量之上限為0.05%。An element necessary for refining N-type crystal grains. The fine nitride system increases the nucleation site at the time of recrystallization, and has an effect of suppressing the growth of crystal grains. In order to exert this effect, the content of N is 0.002% or more. When the N content is significantly larger than 0.005% or more of the general level, the effect of suppressing the growth of crystal grains is more remarkable. This effect is more preferably increased to 0.01% or more, and more preferably 0.02% or more, since the content of N is increased as the content of N increases. In particular, when the amount of C is less than 0.005%, the effect obtained by the addition of such N is more intense. On the other hand, when added more than 0.05%, the elongation at break is remarkably lowered. Therefore, the upper limit of the content of N is 0.05%.
Cu係促成析出強化之重要的元素。小於0.5%時，完全固熔於鋼中，無法得到析出強化之效果，故Cu含量之下限為0.5%。上限因考慮到使強度飽和作為3.0%。The Cu system promotes an important element for precipitation strengthening. When it is less than 0.5%, it is completely solid-melted in steel, and the effect of precipitation strengthening cannot be obtained, so the lower limit of the Cu content is 0.5%. The upper limit is considered to make the intensity saturation 3.0%.
Ni係有效於使鋼板不太過分脆化且可高度強化之元素。但是，由於價格高昂，因應強度之需要添加即可。添加時，為充分得到該強度，以含有0.5%以上為佳。又，上限因考慮到成本作為3.0%。又，從添加Cu引發之剝離瑕疵之觀點言，以添加Cu添加量之½以上為佳。The Ni system is effective for an element which makes the steel sheet less excessively brittle and highly reinforced. However, due to the high price, it can be added in response to the intensity. When it is added, in order to sufficiently obtain the strength, it is preferable to contain 0.5% or more. In addition, the upper limit is 3.0% due to consideration of cost. Further, from the viewpoint of the addition of Cu-induced exfoliation, it is preferable to add 1⁄2 or more of the Cu addition amount.
Sn係改善聚集組織，又，具有抑制退火時之氮化或氧化的效果。特別是改善因添加Cu使磁束密度降低之效果大。為發揮該等之效果時，小於0.01%時，無法得到期望之效果，另一方面，添加大於0.10%，則引起剝離增大。因此，Sn之添加量以0.01%以上、0.10%以下為佳。Sn improves the aggregate structure and has the effect of suppressing nitridation or oxidation during annealing. In particular, it is effective to improve the effect of reducing the magnetic flux density by adding Cu. In order to exhibit the effect of the above, when the effect is less than 0.01%, the desired effect cannot be obtained. On the other hand, when the addition is more than 0.10%, the peeling is increased. Therefore, the amount of addition of Sn is preferably 0.01% or more and 0.10% or less.
B係於粒界偏析，有提高熱軋板及熱軋退火板之韌性的 效果。為發揮該效果時，於0.0010%時，無法得到期望的效果，另一方面，添加大於0.0050%，則發生鑄造時之平板破裂。因此，B之添加量以0.0010%以上、0.0050%以下為佳。B is segregated at the grain boundary and has improved toughness of hot rolled sheets and hot rolled annealed sheets. effect. In order to exhibit this effect, the desired effect cannot be obtained at 0.0010%. On the other hand, when the addition is more than 0.0050%, the flat plate is broken during casting. Therefore, the amount of addition of B is preferably 0.0010% or more and 0.0050% or less.
Nb、Zr、Ti及V之4元素，具有生成碳化物或氮化物，抑制結晶粒粗大化之效果。因此，滿足於用為以各元素的質量%除以原子量之值構成之通式(1)時，發現有顯著的效果。[NB]係表示Nb之含量(質量%)，[Zr]係表示Zr之含量(質量%)，[Ti]係表示Ti之含量(質量%)，[V]係表示V之含量(質量%)。The four elements of Nb, Zr, Ti, and V have the effect of forming carbides or nitrides and suppressing coarsening of crystal grains. Therefore, it is found to have a remarkable effect when it is satisfied that the formula (1) is composed by dividing the mass % of each element by the atomic weight. [NB] indicates the content of Nb (% by mass), [Zr] indicates the content of Zr (% by mass), [Ti] indicates the content of Ti (% by mass), and [V] indicates the content of V (% by mass). ).
2.0×10-4 ≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51……(1)2.0×10 -4 ≦[Nb]/93+[Zr]/91+[Ti]/48+[V]/51......(1)
通式(1)中，右邊之值小於2.0×10-4 時，析出量不足，無法得到充分的結晶粒抑制之效果。因此，右邊之值的下限為2.0×10-4 。另一方面，該等之元素的過量含有分，在鋼中固熔，由於不會影響到鋼之特性，故上限未特予規定。但是，考慮到特性及成本，則右邊之值以1.0×10-2 以下為佳。In the general formula (1), when the value on the right side is less than 2.0 × 10 -4 , the amount of precipitation is insufficient, and sufficient effect of suppressing crystal grains cannot be obtained. Therefore, the lower limit of the value on the right side is 2.0 × 10 -4 . On the other hand, the excessive content of these elements is solid-melted in the steel, and since the characteristics of the steel are not affected, the upper limit is not specified. However, considering the characteristics and cost, the value on the right side is preferably 1.0 × 10 -2 or less.
規定C、N、Nb、Zr、Ti、及V的6元素之通式(2)，係與通式(1)聯合使結晶粒微細化之重要參數。[C]係表示C含量(質量%)，[N]係表示N含量(質量%)。The general formula (2) which defines six elements of C, N, Nb, Zr, Ti, and V is an important parameter for synthesizing crystal grains in combination with the general formula (1). [C] represents C content (% by mass), and [N] represents N content (% by mass).
1.0×10-3 ≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10-3 ……(2)1.0×10 -3 ≦[C]/12+[N]/14-([Nb]/93+[Zr]/91+[Ti]/48+[V]/51)≦3.0×10 -3 ... …(2)
通式(1)係僅規定碳化物或氮化物所能生成的最大量者，僅藉由該條件無法充分抑制最終退火之結晶粒成長。The general formula (1) only defines the maximum amount that can be formed by carbides or nitrides, and the crystal grain growth of the final annealing cannot be sufficiently suppressed only by such conditions.
通式(2)之第2項，係從C及N之質量%除以原子量之值的總和，減去通式(1)之右邊者，係表示不會形成碳氮化物 之過量的C量及/或N量之參數。The second term of the general formula (2) is the sum of the mass % of C and N divided by the atomic weight, and subtracting the right side of the general formula (1) means that no carbonitride is formed. The parameter of the excess amount of C and/or the amount of N.
該過量之C及/或N，係結晶粒微細化上極為重要。因為，含有過量的C及/或N時，碳氮化物係從精加工退火前適度地分散析出，可確實地抑制退火時之結晶粒成長。It is extremely important that the excess C and/or N is a fine grain of crystal grains. When an excessive amount of C and/or N is contained, the carbonitride is appropriately dispersed and precipitated before finishing annealing, and the growth of crystal grains during annealing can be surely suppressed.
在本發明中，碳化物、氮化物及碳氮化物，雖扮演極為重要之任務，其中亦以氮化物及碳氮化物有用，特別是氮化物具有顯著的效果。即，比較碳化物與氮化物，則屬於氮化物者對於本發明之效果是有效的，而屬於氮化物者以少量發揮有助於本發明之效果之作用。又，以同量之碳化物與氮化物比較，則屬於氮化物者可得到大幅度的良好效果，且可抑制不良之副作用。此處所謂「良好效果」係指結晶粒之微細化、高強度化、高溫中的穩定性之意。所謂「不良之副作用」係指鐵損之上昇，以析出物為起點之龜裂(特別是脆化)之意。In the present invention, carbides, nitrides, and carbonitrides play an extremely important task, and are also useful as nitrides and carbonitrides, and particularly nitrides have a remarkable effect. That is, when carbides and nitrides are compared, those belonging to the nitride are effective for the effects of the present invention, and those belonging to the nitride exhibit a small amount of effects contributing to the effects of the present invention. Further, when the same amount of carbides and nitrides are used, it is possible to obtain a large-scale good effect as a nitride, and it is possible to suppress adverse side effects. Here, the "good effect" means the refinement of the crystal grains, the increase in strength, and the stability in high temperature. The term "bad side effects" refers to the rise of iron loss and the meaning of cracks (especially embrittlement) starting from precipitates.
藉由該類析出物之種類而變化的無方向性電磁鋼板的特性之機序，雖尚未明確，認為係受到析出物之大小，形態(異方性)，與基相之整合性，析出物之場所等之影響。又，認為該等的析出物之大小等係受到構成元素之溶解度的差異，析出物之結晶構造的不同，構成原子大小之差別等之影響。The sequence of the characteristics of the non-oriented electrical steel sheet which is changed by the type of the precipitate is not clear, and it is considered that the size of the precipitate, the form (heterogeneity), the integration with the base phase, and the precipitate The influence of places, etc. In addition, it is considered that the size of the precipitates is affected by the difference in solubility of the constituent elements, and the difference in crystal structure of the precipitates affects the difference in atom size.
如此，不僅是Nb、Zr、Ti及V之含量，由於考慮到與含C量之平衡及製造步驟中之熱經歷，而使N含量適當之緣故，在本發明中，氮化物之形成優先於傳統之電磁鋼板。該結果，在高溫中結晶粒成長被抑制，故可抑制鐵損之上 昇及脆化。Thus, not only the contents of Nb, Zr, Ti, and V, but the N content is appropriate in consideration of the balance with the amount of C and the thermal history in the manufacturing step, in the present invention, the formation of nitride takes precedence over Traditional electromagnetic steel sheet. As a result, crystal grain growth is suppressed at a high temperature, so that iron loss can be suppressed. Rise and embrittlement.
再者，關於碳氮化物，由於因應形成之過程其構成成為多種，故其特性及作用雖無法一概而論，至少比僅由碳化物構成之析出物顯示出良好之作用。因此，C含量對N含量之比例以高為佳，以[N]/[C]為3以上為佳，而較佳為5以上。又，氮化物之構成，例如，係認為因有無將碳化物作為初期形成物，或有無將氮化物作為初期形成物，或於成長之過程有無具有類似碳化物之構造，或於成長之過程有無具有類似氮化物之構造等之影響而變化。Further, since the carbonitride has a variety of constitutions due to the formation process, the characteristics and effects thereof cannot be generalized, and at least exhibit a good effect than the precipitate composed only of carbides. Therefore, the ratio of the C content to the N content is preferably high, and [N]/[C] is preferably 3 or more, and more preferably 5 or more. Further, the composition of the nitride is, for example, considered to be whether or not the carbide is used as an initial formation, whether or not the nitride is used as an initial formation, or whether there is a structure having a similar carbide during growth, or whether it is grown or not. It changes with the influence of a nitride-like structure or the like.
通式(2)之第2項之值(參數值)小於1.0×10-3 時，碳氮化物之熱穩定性減弱。例如，在即將精加工退火之再結晶前析出，使再結晶延遲，更提高退火溫度，則析出物再固熔，結晶粒粗大化，難於形成穩定的微細粒。另一方面，參數值大於3.0×10-3 之水準為止，C及/或N過量時，在冷卻中產生淬火，使鋼板之展延及韌性發生劣化。When the value (parameter value) of the second term of the general formula (2) is less than 1.0 × 10 -3 , the thermal stability of the carbonitride is weakened. For example, it is precipitated before the recrystallization of the finish annealing to delay the recrystallization, and the annealing temperature is further increased, whereby the precipitates are resolidified, and the crystal grains are coarsened, and it is difficult to form stable fine particles. On the other hand, when the parameter value is greater than the level of 3.0 × 10 -3 , when C and / or N is excessive, quenching occurs during cooling, and the elongation and toughness of the steel sheet are deteriorated.
根據以上的理由，通式(2)之參數值之下限為1.0×10-3 ，上限作為3.0×10-3 。For the above reasons, the lower limit of the parameter value of the general formula (2) is 1.0 × 10 -3 , and the upper limit is 3.0 × 10 -3 .
高強度無方向性電磁鋼板本身之再結晶面積率小於50%時，製品特性，特別是破斷伸長率顯著地降低。因此，該再結晶面積率作為50%以上。When the recrystallization area ratio of the high-strength non-oriented electrical steel sheet itself is less than 50%, the product characteristics, particularly the elongation at break, are remarkably lowered. Therefore, the recrystallization area ratio is 50% or more.
拉伸試驗之降伏應力，考慮高速旋轉之轉子必要之強度作為700MPa。又，在此規定之降伏應力係指下降伏點。The tensile stress of the tensile test, considering the necessary strength of the rotor rotating at high speed, is 700 MPa. Further, the stress at which the stress is specified herein means a falling point.
破斷伸長率，從抑制馬達芯鑿穿端面之龜裂的觀點 言，作為10%以上。Breaking elongation, from the viewpoint of suppressing cracking of the end face of the motor core Say, as 10% or more.
渦流損失係於激磁時，電流於鋼板上流動所產生之損失，該損失大時，馬達芯易於發熱而引起磁石之減磁。渦流損失We10/400 ，由於對鋼板之板厚的依存性大，故以板厚t(mm)作為參數，而作為轉子發熱之容許範圍如通式(3)所示為70×t2 以下。The eddy current loss is a loss caused by the current flowing on the steel sheet during the excitation, and when the loss is large, the motor core is prone to heat generation and causes magnetism demagnetization. Since the eddy current loss We 10/400 has a large dependence on the thickness of the steel sheet, the thickness t (mm) is used as a parameter, and the allowable range of the heat generation of the rotor is 70 × t 2 or less as shown in the general formula (3). .
We10/400 ≦70×t2 ……(3)We 10/400 ≦70×t 2 ......(3)
該渦流損失之計算方法係使用二周波法。例如，在1.0T之最大磁束密度Bmax的周波數f1 之鐵損為W1 ，而周波數f2 之鐵損為W2 ，則We10/400 之渦流損失We10/400 ，可用「(W2 /f2 -W1 /f1 )/(f2 -f1 )×400×400」計算。The calculation method of the eddy current loss uses a two-cycle method. For example, the maximum magnetic flux density Bmax is the number of cycles of 1.0T f 1 of the iron loss of W 1, f 2 and the cycle number of the iron loss W 2, the eddy current loss We 10/400 10/400 of We, the available "( W 2 /f 2 -W 1 /f 1 )/(f 2 -f 1 )×400×400” is calculated.
在1.0T之最大磁束密度Bmax，如有周波數不同之複數的鐵損值，由於可計算對測定周波數未特予規定。但儘可能在近於400Hz之周波數，例如，以約在100~800Hz之周波數範圍計算為佳。又，最大磁束密度Bmax係於鐵損測定時激磁之最大磁束密度。At a maximum magnetic flux density Bmax of 1.0T, if there is a complex iron loss value having a different number of cycles, the number of measurement cycles is not specified. However, it is preferable to calculate the number of cycles near 400 Hz as much as possible, for example, in the range of the number of cycles of about 100 to 800 Hz. Further, the maximum magnetic flux density Bmax is the maximum magnetic flux density of the excitation at the time of iron loss measurement.
其次，敘述有關於本發明相關之高強度無方向性電磁鋼板製造方法中的數值之限定理由。Next, the reason for limiting the numerical values in the method for producing a high-strength non-oriented electrical steel sheet according to the present invention will be described.
精加工退火係使Cu一旦固熔，且藉由冷卻中析出得到高強度。因此，精加工退火之均熱溫度T(℃)須於Cu之固熔溫度以上。該固熔溫度係依存於Cu之含量。Cu含量作為a(質量%)時，如有200×a+500之溫度(℃)以上，則Cu可完全固熔，故如通式(4)所示精加工退火之均熱溫度T為200×a+500以上。Finishing annealing allows Cu to be solid-melted and precipitated by cooling to obtain high strength. Therefore, the soaking temperature T (°C) of the finishing annealing must be above the solidification temperature of Cu. The solid solution temperature depends on the content of Cu. When the Cu content is a (% by mass), if the temperature is 200×a+500 (°C) or more, Cu can be completely solid-melted, so the soaking temperature T of the finishing annealing as shown in the general formula (4) is 200. ×a+500 or more.
T≧200×a+500以上……(4)T≧200×a+500 or more......(4)
熱軋時之捲取溫度大於550℃，則碳氮化物及Cu析出物，由於熱軋板顯著地降低其韌性。因此，熱軋時之捲取溫度為550℃以下。關於熱軋板之韌性，從冷軋時之破斷抑制的觀點言，夏丕氏衝擊試驗之延性脆性斷面轉移溫度為70℃以下。When the coiling temperature at the time of hot rolling is more than 550 ° C, the carbonitride and the Cu precipitate are remarkably lowered in toughness due to the hot rolled sheet. Therefore, the coiling temperature at the time of hot rolling is 550 ° C or less. Regarding the toughness of the hot rolled sheet, from the viewpoint of the suppression at the time of cold rolling, the ductile brittle fracture transition temperature of the Charpy impact test was 70 ° C or lower.
關於熱軋板之退火，從900℃至500℃之冷卻速度，低於50℃/秒鐘，則由於碳氮化物或Cu析出物，熱軋退火板之韌性顯著降低。因此，在該溫度範圍之冷卻速度為50℃/秒鐘。關於退火後之鋼板的韌性，從冷軋時之破斷抑制觀點言，夏丕氏衝擊試驗時之延性脆性斷面轉移溫度為70℃以下。Regarding the annealing of the hot rolled sheet, the cooling rate from 900 ° C to 500 ° C is less than 50 ° C / sec, and the toughness of the hot rolled annealed sheet is remarkably lowered due to carbonitride or Cu precipitate. Therefore, the cooling rate in this temperature range is 50 ° C / sec. Regarding the toughness of the steel sheet after annealing, the ductile brittle fracture temperature at the Charpy impact test was 70 ° C or less from the viewpoint of the suppression at the time of cold rolling.
再者，關於熱軋板之退火溫度，雖未特予規定，從熱軋板之退火目的為熱軋板之再結晶及促進粒成長而言，以900℃以上為佳，另一方面，從脆性觀點言，以1100℃以下為佳。In addition, the annealing temperature of the hot-rolled sheet is not particularly specified, and the annealing target of the hot-rolled sheet is preferably 900 ° C or higher for recrystallization of the hot-rolled sheet and promotion of grain growth. The brittle view is preferably 1100 ° C or less.
此處規定之轉移溫度，如同日本工業規格(JIS)所規定，在表示試驗溫度及延性斷面率之關係的轉移曲線中，延性斷面率為50%之溫度。亦可採用對應於延性斷面率為0%及100%時所吸收熱量平均值之溫度。The transfer temperature specified herein is a temperature of 50% in the transfer curve indicating the relationship between the test temperature and the ductile cross-sectional rate as specified by the Japanese Industrial Standards (JIS). It is also possible to use a temperature corresponding to the average value of the absorbed heat when the ductility section ratio is 0% and 100%.
用於夏丕氏衝擊試驗之試驗片的長度及高度，則以JIS所規定之大小。另一方面，試驗片之寬度，則以熱軋板之厚度。因此，作為大小則於壓延方向之長度55毫米、高度10毫米，寬度則因應熱軋板之厚度約1.5毫米至3.0毫米。更於試驗時，重疊複數片之試驗片，以使成為近於正規試驗條件之厚度10毫米為佳。The length and height of the test piece used for the Charpy impact test are as specified by JIS. On the other hand, the width of the test piece is the thickness of the hot rolled sheet. Therefore, the size is 55 mm in length and 10 mm in height in the rolling direction, and the width is about 1.5 mm to 3.0 mm in response to the thickness of the hot rolled sheet. Further, in the test, the test pieces of a plurality of sheets were overlapped so that a thickness of 10 mm which is close to the normal test condition is preferable.
在真空熔解爐中，以質量%計，製造含有Si：2.9%、Mn：0.2%、Al：0.7%及Cu：1.5%，且C、N、Nb、Zr、Ti及V之質量%不同之鋼，在1150℃加熱60分鐘後，立即熱軋，得到板厚為2.3毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中得到板厚為0.5毫米之冷軋板。對於該冷軋板，在900℃實施60秒鐘之精加工退火。第5表中顯示成分及諸特性之測定結果。In the vacuum melting furnace, Si: 2.9%, Mn: 0.2%, Al: 0.7%, and Cu: 1.5% are produced in mass%, and the mass % of C, N, Nb, Zr, Ti, and V are different. The steel, after heating at 1,150 ° C for 60 minutes, was immediately hot rolled to obtain a hot rolled sheet having a thickness of 2.3 mm. Then, the hot rolled sheet was subjected to pickling, and a cold rolled sheet having a thickness of 0.5 mm was obtained in one cold rolling. For this cold-rolled sheet, finishing annealing was performed at 900 ° C for 60 seconds. The measurement results of the components and the characteristics are shown in Table 5.
在不能滿足通式(1)之符號a1中，降伏應力及渦流損失We10/400 不符合本發明所規定之範圍。又，在不能滿足通式(2)之符號a14~a17中，再結晶率及破斷伸長率不符合本發明所規定之範圍。C含量大於本發明所規定的範圍之上限，且在不能滿足通式(2)之符號a20中，破斷伸長率不符合本發明所規定之範圍。各要件符合本發明所規定的範圍內之其他試樣(符號a2、a3及a18)中得到良好之特性。In the symbol a1 in which the general formula (1) cannot be satisfied, the fall stress and the eddy current loss We 10/400 do not conform to the range specified by the present invention. Further, in the symbols a14 to a17 which do not satisfy the general formula (2), the recrystallization ratio and the breaking elongation do not conform to the range defined by the present invention. The C content is larger than the upper limit of the range specified by the present invention, and in the case of the symbol a20 which does not satisfy the general formula (2), the breaking elongation does not conform to the range specified by the present invention. Good characteristics are obtained in the other samples (symbols a2, a3, and a18) in which the respective requirements are within the range specified by the present invention.
在真空熔解爐中，以質量%計，製造含有Si：3.7%、Mn：0.1%、Al：0.2%及Cu：1.4%，且C、N、Nb、Zr、Ti及V之質量%不同之鋼，在1150℃加熱60分鐘後，立即熱軋，得到板厚為2.3毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中得到板厚為0.5毫米之冷軋板。對於該冷軋板，在900℃實施60秒鐘之精加工退火。第6表中顯示成分及諸特性之測定結果。In the vacuum melting furnace, Si: 3.7%, Mn: 0.1%, Al: 0.2%, and Cu: 1.4% are produced in mass%, and the mass % of C, N, Nb, Zr, Ti, and V are different. The steel, after heating at 1,150 ° C for 60 minutes, was immediately hot rolled to obtain a hot rolled sheet having a thickness of 2.3 mm. Then, the hot rolled sheet was subjected to pickling, and a cold rolled sheet having a thickness of 0.5 mm was obtained in one cold rolling. For this cold-rolled sheet, finishing annealing was performed at 900 ° C for 60 seconds. The measurement results of the components and the characteristics are shown in the sixth table.
在不能滿足通式(1)之符號b1中，降伏應力及渦流損失We10/400 不符合本發明所規定之範圍。又，在不能滿足通式(2)之符號b14~b17中，再結晶率及破斷伸長率不符合本發明所規定之範圍。同樣地，在不能滿足通式(2)之符號b20中，破斷伸長率不符合本發明所規定之範圍。各要件符合本發明所規定的範圍內之其他試樣(符號b2、b3及b18)中得到良好之特性。In the symbol b1 in which the general formula (1) cannot be satisfied, the lodging stress and the eddy current loss We 10/400 do not conform to the range specified by the present invention. Further, in the case of not satisfying the symbols b14 to b17 of the general formula (2), the recrystallization ratio and the breaking elongation do not conform to the range defined by the present invention. Similarly, in the symbol b20 in which the general formula (2) cannot be satisfied, the breaking elongation does not conform to the range defined by the present invention. Good characteristics are obtained in the other samples (symbols b2, b3 and b18) in which the requirements are within the range specified by the present invention.
在真空熔解爐中，以質量%計，製造含有C：0.022%、Mn：0.5%、Al：2.0%、N：0.003%、Ni：1.0%、Nb：0.031%、Zr：0.004%、Ti：0.003%及V：0.004%，且變化Si量及Cu量之鋼，在1120℃加熱120分鐘後立即熱軋，得到板厚為2.0毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中得到板厚為0.5毫米之冷軋板。對於該冷軋板，在1000℃實施45秒鐘之精加工退火。第6表中顯示Si量、Cu量及諸特性之測定結果。In the vacuum melting furnace, C: 0.022%, Mn: 0.5%, Al: 2.0%, N: 0.003%, Ni: 1.0%, Nb: 0.031%, Zr: 0.004%, Ti: in terms of % by mass. 0.003% and V: 0.004%, and the steel in which the amount of Si and the amount of Cu were changed, and hot-rolled immediately after heating at 1,120 ° C for 120 minutes to obtain a hot-rolled sheet having a thickness of 2.0 mm. Then, the hot rolled sheet was subjected to pickling, and a cold rolled sheet having a thickness of 0.5 mm was obtained in one cold rolling. For this cold-rolled sheet, finishing annealing was performed at 1000 ° C for 45 seconds. The measurement results of the amount of Si, the amount of Cu, and various characteristics are shown in Table 6.
在不能滿足通式(1)之符號b1中，降伏應力及渦流損失We10/400 不符合本發明所規定之範圍。又，在不能滿足通式(2)之符號b14~b17中，再結晶率及破斷伸長率不符合本發明所規定之範圍。同樣地，在不能滿足通式(2)之符號b20中，破斷伸長率不符合本發明所規定之範圍。各要件符合本發明所規定的範圍內之其他試樣(符號b2、b3、b18及b19)中得到良好之特性。In the symbol b1 in which the general formula (1) cannot be satisfied, the lodging stress and the eddy current loss We 10/400 do not conform to the range specified by the present invention. Further, in the case of not satisfying the symbols b14 to b17 of the general formula (2), the recrystallization ratio and the breaking elongation do not conform to the range defined by the present invention. Similarly, in the symbol b20 in which the general formula (2) cannot be satisfied, the breaking elongation does not conform to the range defined by the present invention. Good characteristics were obtained in the other samples (symbols b2, b3, b18, and b19) in which the respective requirements were within the range specified by the present invention.
在真空熔解爐中，以質量%計，製造含有C：0.022%、Mn：0.5%、Al：2.0%、N：0.003%、Ni：1.0%、Nb：0.031%、Zr：0.004%、Ti：0.003%及V：0.004%，且變化Si量及Cu量之鋼，在1120℃加熱120分鐘後立即熱軋，得到板厚為2.0毫米之熱軋板。然後，該熱軋板實施酸洗，在一次之冷軋中得到板厚為0.5毫米之冷軋板。對於該冷軋板，在1000℃實施45秒鐘之精加工退火。第6表中顯示Si量、Cu量及諸特性之測定結果。In the vacuum melting furnace, C: 0.022%, Mn: 0.5%, Al: 2.0%, N: 0.003%, Ni: 1.0%, Nb: 0.031%, Zr: 0.004%, Ti: in terms of % by mass. 0.003% and V: 0.004%, and the steel in which the amount of Si and the amount of Cu were changed, and hot-rolled immediately after heating at 1,120 ° C for 120 minutes to obtain a hot-rolled sheet having a thickness of 2.0 mm. Then, the hot rolled sheet was subjected to pickling, and a cold rolled sheet having a thickness of 0.5 mm was obtained in one cold rolling. For this cold-rolled sheet, finishing annealing was performed at 1000 ° C for 45 seconds. The measurement results of the amount of Si, the amount of Cu, and various characteristics are shown in Table 6.
Si之含量低於本發明所規定範圍之1.8%的試樣(符號c1~c5)中，降伏應力及渦流損失We10/400 ，不符合本發明所規定之範圍。又，Si之含量大於本發明所規定之範圍之4.1%的試樣(符號c21~c25)中，破斷伸長率顯著地低。In the samples (symbols c1 to c5) in which the content of Si is less than 1.8% of the range specified in the present invention, the stress of undulation and the eddy current loss We 10/400 do not conform to the range specified by the present invention. Further, in the samples (symbols c21 to c25) in which the content of Si was larger than 4.1% of the range specified in the present invention, the elongation at break was remarkably low.
再者，Si之含量雖於本發明所規定之範圍，在Cu小於0.5%之試樣(符號c6、c11及c16)中降伏應力低，不符合本發明所規定之範圍。又，對於鎳/Cu為0.5%以上之試樣(符號c1~c4、c6~c9、c11~c14、c16~c19及c21~c24)，未發現結疤。Further, although the content of Si is within the range specified by the present invention, the stress at which the Cu is less than 0.5% (symbols c6, c11 and c16) has a low stress, which does not conform to the range specified by the present invention. Further, for samples in which nickel/Cu was 0.5% or more (symbols c1 to c4, c6 to c9, c11 to c14, c16 to c19, and c21 to c24), no crucible was found.
在真空熔解爐中，以質量%計，製造含有C：0.003%、Si：3.3%、Mn：0.2%、Al：0.7%、N：0.022%、Ni：1.5%、Nb：0.032%、Zr：0.004%、Ti：0.003%及V：0.003%，且變化B量及Sn量之鋼，在1110℃加熱80分鐘後，立即熱軋，得到板厚為2.7毫米之熱軋板。在熱軋中之捲取溫度為530℃。然後，該熱軋板於1050℃實施60秒鐘之退火(中間退火)，更實施酸洗，在一次之冷軋中得到板厚為0.35毫米之冷軋板。對於該冷軋板，在950℃實施60秒鐘之精加工退火。第8表中顯示B量、Sn量、中間退火後之轉移溫度及精加工退火後之磁束密度。In the vacuum melting furnace, C: 0.003%, Si: 3.3%, Mn: 0.2%, Al: 0.7%, N: 0.022%, Ni: 1.5%, Nb: 0.032%, Zr: 0.004%, Ti: 0.003%, and V: 0.003%, and the steel having the amount of change B and the amount of Sn was heated at 1110 ° C for 80 minutes, and immediately hot rolled to obtain a hot rolled sheet having a thickness of 2.7 mm. The coiling temperature in hot rolling was 530 °C. Then, the hot rolled sheet was annealed at 6050 ° C for 60 seconds (intermediate annealing), and further subjected to pickling, and a cold rolled sheet having a thickness of 0.35 mm was obtained in one cold rolling. For this cold-rolled sheet, finishing annealing was performed at 950 ° C for 60 seconds. In Table 8, the amount of B, the amount of Sn, the transfer temperature after the intermediate annealing, and the magnetic flux density after finishing annealing are shown.
B量為0.0010%以上之符號d6~d25中，熱軋退火之轉移溫度低。Sn量為0.010%以上之符號d2~d5、d7~d10，d12~d15、d17~20及符號d21~25中得到高磁束密度。又，B量大於0.0050%以上之符號d21~d25中發生平板破損，錫量大於0.010%之符號d5、d10、d15、d20及d25發生鑄疵。In the symbol d6 to d25 in which the amount of B is 0.0010% or more, the transfer temperature of the hot rolling annealing is low. A high magnetic flux density is obtained in the symbols d2 to d5, d7 to d10, d12 to d15, d17 to 20, and d21 to 25 in which the amount of Sn is 0.010% or more. Further, when the amount of B is more than 0.0050% or more, the plate d21 to d25 is broken, and the symbols d5, d10, d15, d20, and d25 in which the amount of tin is more than 0.010% are cast.
在真空熔解爐中，以質量%計，製造含有C：0.028%、Si：2.9%、Mn：0.8%、Al：1.4%、N：0.012%、Ni：1.4%、Nb：0.03%、Zr：0.04%、Ti：0.003%及V：0.003%，且變化Cu量之鋼，在1120℃加熱90分鐘後立即熱軋，得到板厚為2.0毫米之熱軋板。然後，該熱軋板於950℃實施60秒鐘之熱軋板退火，更實施酸洗，在一次之冷軋中得到板厚為0.35毫米之冷軋板。在該冷軋板上，變化均熱溫度實施精加工退火。第9表中顯示Cu量，精加工退火之溫度諸特性之結果。In the vacuum melting furnace, C: 0.028%, Si: 2.9%, Mn: 0.8%, Al: 1.4%, N: 0.012%, Ni: 1.4%, Nb: 0.03%, Zr: 0.04%, Ti: 0.003%, and V: 0.003%, and the steel having a varying amount of Cu was hot-rolled immediately after heating at 1,120 ° C for 90 minutes to obtain a hot rolled sheet having a thickness of 2.0 mm. Then, the hot rolled sheet was annealed at 950 ° C for 60 seconds, and further subjected to pickling, and a cold rolled sheet having a thickness of 0.35 mm was obtained in one cold rolling. On the cold-rolled sheet, finishing annealing is performed by changing the soaking temperature. Table 9 shows the results of the characteristics of the amount of Cu and the temperature of the finish annealing.
均熱溫度滿足通式(4)之試樣(符號e1、e13~e15、e18~e20及e25)中，降伏應力、破斷伸長率及渦流損失We10/400 均在本發明所規定之範圍，故得到良好之特性。In the samples in which the soaking temperature satisfies the formula (4) (symbols e1, e13 to e15, e18 to e20, and e25), the relief stress, the elongation at break, and the eddy current loss We 10/400 are all within the scope of the present invention. Therefore, good characteristics are obtained.
均熱溫度未能滿足通式(4)之試樣(符號e11、e12、e16、e17、e21~e24)中，再結晶面積率小於50%及/或破斷伸長率小於10%，故不符合本發明所規定之範圍。If the soaking temperature fails to satisfy the sample of the formula (4) (symbols e11, e12, e16, e17, e21 to e24), the recrystallization area ratio is less than 50% and/or the elongation at break is less than 10%, so Meet the scope of the invention.
在真空熔解爐中，以質量%計，製造含有C：0.027%、Si：3.6%、Mn：0.1%、Al：1.8%、N：0.005%、Ni：2.0%、Nb：0.003%、Zr：0.004%、Ti：0.03%及V：0.01%之複數的鋼片。該等之鋼片於1170℃加熱90分鐘後立即熱軋，得到板厚為2.5毫米之熱軋板。在製作該熱軋板時變化捲取溫 度。更於製造之熱軋板，在1000℃實施60秒鐘之退火得到退火板。在退火時，變化從900℃至500℃之冷卻速度。從該等之熱軋板及退火板，製造夏丕氏試驗片，藉由衝擊試驗測定轉移溫度。該結果顯示於第10表。In the vacuum melting furnace, C: 0.027%, Si: 3.6%, Mn: 0.1%, Al: 1.8%, N: 0.005%, Ni: 2.0%, Nb: 0.003%, Zr: A steel sheet of 0.004%, Ti: 0.03%, and V: 0.01%. These steel sheets were hot rolled immediately after heating at 1,170 ° C for 90 minutes to obtain a hot rolled sheet having a thickness of 2.5 mm. Changing the coiling temperature when making the hot rolled sheet degree. Further, the hot rolled sheet produced was annealed at 1000 ° C for 60 seconds to obtain an annealed sheet. At the time of annealing, the cooling rate from 900 ° C to 500 ° C was varied. From these hot-rolled sheets and annealed sheets, Xia's test pieces were produced, and the transfer temperature was measured by an impact test. The results are shown in Table 10.
在捲取溫度550℃以下之試樣(符號f1~f3)中，得到轉移溫度為70℃以下之優良特性。又，關於退火板，不論捲取溫度，從900℃至500℃之冷卻速度為50℃/秒鐘以上之試樣(符號f8~f10、f13~f15及f18~f20)中，得到轉移溫度為70℃以下之優良特性。In the samples (symbols f1 to f3) having a coiling temperature of 550 ° C or lower, excellent characteristics of a transition temperature of 70 ° C or less were obtained. Further, in the annealed sheet, regardless of the coiling temperature, a sample having a cooling rate of 900 ° C to 500 ° C of 50 ° C /sec or more (symbols f8 to f10, f13 to f15, and f18 to f20) was obtained. Excellent characteristics below 70 °C.
根據本發明可不用犧牲馬達芯或鋼板製造時之成品率或生產性，能以低成本提供強度優異之無方向性電磁鋼板。According to the present invention, it is possible to provide a non-oriented electrical steel sheet excellent in strength at a low cost without sacrificing the yield or productivity at the time of manufacture of a motor core or a steel sheet.
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| JP4415933B2 (en) * | 2005-12-15 | 2010-02-17 | 住友金属工業株式会社 | Method for producing non-oriented electrical steel sheet for rotor |
| EP2031079B1 (en) * | 2006-06-16 | 2021-01-13 | Nippon Steel Corporation | High-strength electromagnetic steel sheet and process for producing the same |
-
2009
- 2009-04-13 PL PL09732579T patent/PL2278034T3/en unknown
- 2009-04-13 US US12/922,772 patent/US20110056592A1/en not_active Abandoned
- 2009-04-13 WO PCT/JP2009/057453 patent/WO2009128428A1/en active Application Filing
- 2009-04-13 BR BRPI0910984A patent/BRPI0910984B8/en active IP Right Grant
- 2009-04-13 JP JP2010508206A patent/JP4659135B2/en active Active
- 2009-04-13 CN CN2009801130902A patent/CN102007226B/en active Active
- 2009-04-13 EP EP09732579.9A patent/EP2278034B1/en active Active
- 2009-04-13 KR KR1020107022839A patent/KR20100122116A/en not_active Application Discontinuation
- 2009-04-14 TW TW098112291A patent/TWI404806B/en active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20060124207A1 (en) * | 2002-12-05 | 2006-06-15 | Jfe Steel Corporation | Non-oriented magnetic steel sheet and method for production thereof |
| TWI293332B (en) * | 2003-10-06 | 2008-02-11 | Nippon Steel Corp | A high-strength non-oriented electrical steel sheet and a fabricated part and a method of producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| TW200946695A (en) | 2009-11-16 |
| BRPI0910984A2 (en) | 2016-01-05 |
| EP2278034B1 (en) | 2020-02-12 |
| BRPI0910984B1 (en) | 2018-06-05 |
| EP2278034A4 (en) | 2017-01-25 |
| EP2278034A1 (en) | 2011-01-26 |
| CN102007226B (en) | 2013-11-06 |
| BRPI0910984B8 (en) | 2018-09-25 |
| CN102007226A (en) | 2011-04-06 |
| PL2278034T3 (en) | 2020-06-29 |
| WO2009128428A1 (en) | 2009-10-22 |
| KR20100122116A (en) | 2010-11-19 |
| JP4659135B2 (en) | 2011-03-30 |
| US20110056592A1 (en) | 2011-03-10 |
| JPWO2009128428A1 (en) | 2011-08-04 |
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