JP2008240104A - High-strength non-oriented electromagnetic steel sheet and method for producing the same - Google Patents
High-strength non-oriented electromagnetic steel sheet and method for producing the same Download PDFInfo
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本発明は、高強度無方向性電磁鋼板とその製造方法に関し、特に高速回転機のロータやステータコアに用いて好適な、高周波鉄損が低い高強度無方向性電磁鋼板とその製造方法に関するものである。 The present invention relates to a high-strength non-oriented electrical steel sheet and a manufacturing method thereof, and more particularly to a high-strength non-oriented electrical steel sheet having a low high-frequency iron loss and a manufacturing method suitable for use in a rotor and a stator core of a high-speed rotating machine. is there.
近年、モータの駆動制御システムが発達し、駆動電源の周波数制御が可能となったことから、可変速運転や商用周波数域以上で使用される高速回転モータが増加している。回転体に作用する遠心力は、回転半径に比例し、回転速度の２乗に比例して大きくなる。そのため、斯かる高速回転モータ、特に、中・大型の高速回転するモータのロータ材に用いられる電磁鋼板は、高強度であることが必要となる。 In recent years, motor drive control systems have been developed, and frequency control of drive power supply has become possible, and therefore, high-speed motors used in variable speed operation and commercial frequency ranges have increased. The centrifugal force acting on the rotating body is proportional to the radius of rotation and increases in proportion to the square of the rotational speed. Therefore, the electrical steel sheet used for the rotor material of such a high-speed rotating motor, in particular, a medium or large-sized motor that rotates at high speed, needs to have high strength.
また、近年、ハイブリッド自動車の駆動モータやコンプレッサモータなどへの採用が増加している埋め込み磁石型ＤＣインバータ制御モータでは、ロータ部にスリットを設けて磁石を埋設している。そのため、モータ回転時には、狭いブリッジ部（ロータ外周とスリットの間部）に応力が集中するため、ロータに使用されるコア材は高強度であることが要求される。 Further, in recent years, in an embedded magnet type DC inverter control motor, which is increasingly used in a drive motor, a compressor motor, and the like of a hybrid vehicle, a magnet is embedded by providing a slit in a rotor portion. For this reason, when the motor rotates, stress concentrates on a narrow bridge portion (between the outer periphery of the rotor and the slit), so that the core material used for the rotor is required to have high strength.
さらに、モータや発電機などの回転機器は、電磁気現象を利用するものであるため、その鉄心（コア）の素材には、当然のことながら磁気特性に優れることも求められる。特に、高速回転するモータでは、高周波磁束により渦電流が発生し、モータ効率低下の原因となるため、高周波域での鉄損が低いことが重要となる。 Furthermore, since rotating devices such as motors and generators use electromagnetic phenomena, the material of the core (core) is naturally required to have excellent magnetic properties. In particular, in a motor that rotates at high speed, an eddy current is generated by high-frequency magnetic flux and causes a reduction in motor efficiency. Therefore, it is important that the iron loss in a high-frequency region is low.
モータのロータコアには、通常、打ち抜きプレスした無方向性電磁鋼板を積層したものが用いられるが、その鋼板強度が、高速回転するモータに求められる機械強度を満たさない場合には、より高強度な鋳鋼製ロータなどを使用せざるを得ない。しかし、鋳物製ロータは一体物であるため、発生する渦電流損が、電磁鋼板を積層したロータよりも大幅に上昇するという問題がある。従って、高速回転するロータ用素材として、磁気特性に優れかつ高強度な電磁鋼板の開発が望まれている。 For the rotor core of a motor, a laminate of non-oriented electrical steel sheets that have been punched and pressed is usually used.If the steel sheet strength does not meet the mechanical strength required for a motor that rotates at high speed, a higher strength is required. A cast steel rotor must be used. However, since the cast rotor is a single piece, the eddy current loss generated is significantly higher than that of a rotor in which electromagnetic steel sheets are laminated. Accordingly, it is desired to develop a magnetic steel sheet having excellent magnetic properties and high strength as a rotor material that rotates at high speed.
上記要求に応えるため、今日までに高強度無方向性電磁鋼板がいくつか検討され、提案されている。例えば、特許文献１には、Ｓｉ含有量を３．５〜７．０ｍａｓｓ％に高め、さらに固溶強化元素としてＴｉ，Ｗ，Ｍｏ，Ｍｎ，Ｎｉ，Ｃｏ，Ａｌなどを添加して高強度化を図る方法が提案されている。また、特許文献２には、上記強化法に加えて、仕上げ焼鈍条件を工夫することにより、平均結晶粒径を０．０１〜５．０ｍｍとして磁気特性を改善する方法が提案されている。 In order to meet the above requirements, several high-strength non-oriented electrical steel sheets have been studied and proposed to date. For example, in Patent Document 1, the Si content is increased to 3.5 to 7.0 mass%, and further strengthened by adding Ti, W, Mo, Mn, Ni, Co, Al, etc. as solid solution strengthening elements. A method for achieving this has been proposed. Patent Document 2 proposes a method of improving the magnetic characteristics by setting the average crystal grain size to 0.01 to 5.0 mm by devising the finish annealing condition in addition to the above-described strengthening method.
しかしながら、これらの方法は、これを電磁鋼板の実生産に適用した場合には、熱間圧延後の製造ラインで、板破断などのトラブルが発生し易く、歩留まりの低下やラインの生産性の低下を招くなどの問題があった。この問題に対しては、例えば、冷間圧延の場合には、板温を数百℃に昇温制御して温間圧延することにより板破断を軽減することはできるが、温間圧延のための設備が必要となること、製造上の制約が大きいことなどの問題も多い。 However, when these methods are applied to the actual production of electromagnetic steel sheets, troubles such as sheet breakage are likely to occur in the production line after hot rolling, resulting in lower yields and lower line productivity. There was a problem such as inviting. For this problem, for example, in the case of cold rolling, the plate breakage can be reduced by warm-rolling by controlling the temperature of the plate to several hundred degrees Celsius. There are also many problems such as the need for such equipment and the large restrictions on manufacturing.
また、特許文献３には、Ｓｉを２．０ｍａｓｓ％以上４．０ｍａｓｓ％未満含有する鋼に、Ｍｎ，Ｎｉを添加して固溶強化する方法が、特許文献４には、Ｓｉを２．０ｍａｓｓ％以上４．０ｍａｓｓ％未満含有する鋼に、Ｍｎ，Ｎｉを添加して固溶強化し、さらにＮｂ，Ｚｒ，Ｔｉ，Ｖ等の炭窒化物形成元素を添加して、高強度と磁気特性の両立を図る技術が提案されている。しかし、特許文献３の方法では、十分な強度が得られず、また、特許文献４の方法では、高い強度を得られるものの、磁気特性の低下が大きいという問題がある。
Patent Document 3 discloses a method of solid solution strengthening by adding Mn and Ni to a steel containing 2.0 mass% or more and less than 4.0 mass% of Si, and
一方、発明者らは、高Ｓｉ鋼の加工性を改善するための検討を別途行ってきた。その結果、特許文献５に開示したように、無方向性電磁鋼板の基本組成であるＦｅ−Ｓｉ合金やＦｅ−Ｓｉ−Ａｌ合金の加工性（加工性は、ほぼ、靭性によって評価することができる）の向上を図るためには、鋼自体を十分に高純度化し、鋼中のＣ，Ｎを合計量で１００ｍａｓｓｐｐｍ以下に低減した上で、さらに、一定量以上のＣｒを添加することが有効であることを見出した。また、磁気特性に関しても、ＣｒとＳｉまたはＡｌを同時に含有させることにより、電気抵抗の増大に相乗的な効果が現れること、その結果、渦電流損が低減し、特に高周波域での鉄損を、Ｃｒを含有しないＦｅ−Ｓｉ合金やＦｅ−Ａｌ合金、Ｆｅ−Ｓｉ−Ａｌ合金に比べて格段に低減できることを見出している。
上記特許文献５の技術によれば、鋼中のＳｉ濃度を高めることで、高強度でかつ磁気特性にも優れた電磁鋼板を安定して製造することが可能となる。しかし、この技術は、鋼の高純度化を必須の要件としており、特に鋼中のＣとＮは、合計量で０．０１ｍａｓｓ％以下とする必要がある。 According to the technique disclosed in Patent Document 5, an electromagnetic steel sheet having high strength and excellent magnetic properties can be stably manufactured by increasing the Si concentration in the steel. However, this technique requires the high purity of the steel as an essential requirement, and in particular, C and N in the steel need to be 0.01 mass% or less in total amount.
しかしながら、Ｃｒ添加鋼を溶製する場合、添加するＣｒ源（フェロクロムや金属Ｃｒ）には、不純物としてＣが多量に含まれているため、通常のＦｅ−Ｓｉ系の電磁鋼板よりもＣ混入量が多くなる。しかも、Ｃｒは強力な酸化物形成元素であるため、現在の一貫製鉄所で高純度鋼の大量生産に使われているＲＨ（Ｒｕｈｒｓｔａｈｌ−Ｈａｕｓｅｎ）真空脱ガス装置やＬＦ（Ｌａｄｌｅ Ｆｕｒｎａｃｅ）などの２次精錬設備では、Ｃｒ添加後に、Ｃｒの酸化損失を防止しながら極低炭素域まで脱炭するのは難しいという問題がある。例えば、２次精錬装置としてＲＨを用いた場合、２〜５ｍａｓｓ％のＣｒ添加鋼で得られる純度は、Ｃが０．００５〜０．０１ｍａｓｓ％、Ｎが０．００２〜０．００５ｍａｓｓ％程度であり、ＣとＮの合計量で０．０１ｍａｓｓ％以下を安定的に達成するのは難しい。 However, when melting Cr-added steel, the added Cr source (ferrochrome or metallic Cr) contains a large amount of C as an impurity, so the amount of mixed C is higher than that of a normal Fe-Si based electromagnetic steel sheet. Will increase. Moreover, since Cr is a strong oxide-forming element, 2 such as RH (Ruhrstahl-Hausen) vacuum degassing equipment and LF (Laddle Furnace), which are used for mass production of high-purity steel at the present integrated steelworks. In the next refining equipment, there is a problem that it is difficult to decarburize to an extremely low carbon region while preventing oxidation loss of Cr after addition of Cr. For example, when RH is used as a secondary refining device, the purity obtained with 2-5 mass% Cr-added steel is about 0.005-0.01 mass% for C and about 0.002-0.005 mass% for N. In addition, it is difficult to stably achieve 0.01 mass% or less in the total amount of C and N.
なお、Ｃｒ存在下で炭素の優先脱炭を進行させるには、精錬雰囲気中の一酸化炭素分圧を下げることが有効であり、そのためには、ステンレス鋼の製造に用いられているＶＯＤ炉（Ｖａｃｕｕｍ Ｏｘｙｇｅｎ Ｄｅｃａｒｂｕｒｉｚａｔｉｏｎ）やＡＯＤ炉（ＡｒｇｏＮｏ．ｘｙｇｅｎ Ｄｅｃａｒｂｕｒｉｚａｔｉｏｎ）のような特殊な脱ガス精錬設備を用いて長時間の精錬を必要とするため、製造設備が限定されまた生産性が劣るため、製造コストが上昇するといった問題がある。 In order to advance the preferential decarburization of carbon in the presence of Cr, it is effective to lower the partial pressure of carbon monoxide in the refining atmosphere. For that purpose, the VOD furnace (used for the production of stainless steel ( Since long-time refining is required using special degassing refining equipment such as Vacuum Oxygen Decarburization) and AOD furnace (ArgoNo. There is a problem of rising.
上記のように、高強度の無方向性電磁鋼板に関する提案は幾つかなされてはいるものの、現状では、高速回転機器に必要とされる高強度と磁気特性を確保した電磁鋼板を、通常の鋼板製造設備を用いて工業的に安定して製造することは達成できていないのが実情である。 As mentioned above, although several proposals regarding high-strength non-oriented electrical steel sheets have been made, at present, electromagnetic steel sheets that ensure the high strength and magnetic properties required for high-speed rotating equipment are used as ordinary steel sheets. Actually, it has not been possible to achieve industrially stable production using production equipment.
そこで、本発明の目的は、高速回転機器のロータ材等に用いて好適な、高強度で高周波鉄損の低いＣｒ添加高Ｓｉ無方向性電磁鋼板を提供すること、およびその鋼板を、ステンレス鋼で用いられているような特殊な２次精錬設備での長時間処理を必要とすることなく、ＲＨやＬＦといった通常の２次精錬設備を用いて、工業的に安定して高い生産性のもとで製造する方法を提案することにある。 Accordingly, an object of the present invention is to provide a Cr-added high-Si non-oriented electrical steel sheet that is suitable for use as a rotor material of a high-speed rotating device and has a high strength and a low high-frequency iron loss. Without the need for long-time processing in special secondary refining equipment used in the industry, using ordinary secondary refining equipment such as RH and LF, industrially stable and high productivity And to propose a method of manufacturing.
発明者らは、上記課題の解決に向けて、Ｃｒを添加した高Ｓｉ鋼の製造方法に関して種々の実験を行い、検討を重ねた。その結果、Ｃｒ添加とともに一定量のＴｉを添加すれば、通常のＲＨ脱ガス設備で低減できるレベルのＣやＮの純度でも、その後の鋼板製造を安定的に行える加工性（靭性）を付与できること、高強度化と優れた磁気特性を両立させるためには、固溶強化が有効であり、中でもＳｉの添加による固溶強化が有効であることを見出した。そして、上記技術を用いることにより、従来技術では安定製造が難しかった４ｍａｓｓ％を超える高Ｓｉ鋼を、通常の無方向性電磁鋼板の製造設備を用いて安定的に製造することが可能であることを知見し、本発明を開発するに至った。 In order to solve the above-mentioned problems, the inventors conducted various experiments and repeated studies on a method for producing Cr-added high-Si steel. As a result, if a certain amount of Ti is added together with Cr addition, the workability (toughness) can be imparted so that the subsequent steel plate production can be stably performed even with the purity of C and N that can be reduced by ordinary RH degassing equipment. In order to achieve both high strength and excellent magnetic properties, it has been found that solid solution strengthening is effective, and in particular, solid solution strengthening by adding Si is effective. And by using the said technique, it is possible to manufacture stably the high Si steel exceeding 4 mass% which was difficult to manufacture stably by the conventional technique using the manufacturing equipment of a normal non-oriented electrical steel sheet. As a result, the present invention has been developed.
すなわち、本発明は、Ｃ：０．００５０ｍａｓｓ％超０．０２０ｍａｓｓ％以下、Ｎ：０．０１ｍａｓｓ％以下、（Ｃ＋Ｎ）：０．０３０ｍａｓｓ％以下、Ｓｉ：４．０ｍａｓｓ％超１０．０ｍａｓｓ％以下、Ｃｒ：２．０〜１０．０ｍａｓｓ％、Ｐ：０．０４ｍａｓｓ％以下を含有し、さらに、Ｔｉを下記（１）式；
−０．０２≦Ｔｉ−４（Ｃ＋Ｎ）≦０．０４ ・・・（１）
を満たして含有し、残部がＦｅおよび不可避的不純物である高強度無方向性電磁鋼板である。
That is, the present invention is C: more than 0.0050 mass% 0.020 mass% or less, N: 0.01 mass% or less, (C + N): 0.030 mass% or less, Si: more than 4.0 mass%, 10.0 mass% or less, Cr: 2.0-10.0 mass%, P: 0.04 mass% or less is contained, and further Ti is represented by the following formula (1);
−0.02 ≦ Ti-4 (C + N) ≦ 0.04 (1)
Is a high-strength non-oriented electrical steel sheet that contains and balances Fe and unavoidable impurities.
本発明の電磁鋼板は、上記成分組成に加えてさらに、下記Ａ群〜Ｃ群のうちの少なくとも１群の成分を含有することを特徴とする請求項１に記載の高強度無方向性電磁鋼板。
記
Ａ群：ＳｂおよびＳｎのいずれか１種または２種を合計で０．１ｍａｓｓ％以下、
Ｂ群：Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏのいずれか１種または２種以上を合計で５．０ｍａｓｓ％以下、
Ｃ群：Ｃａ，希土類元素（ＲＥＭ）およびＢのいずれか１種または２種以上を合計で０．０１ｍａｓｓ％以下
The high strength non-oriented electrical steel sheet according to claim 1, wherein the electrical steel sheet of the present invention further contains at least one component of the following groups A to C in addition to the above component composition. .
Group A: Any one or two of Sb and Sn in total 0.1 mass% or less,
Group B: Any one or more of Al, Mn, Cu, Mo, Ni and Co in a total of 5.0 mass% or less,
Group C: 0.01 mass% or less of one or more of Ca, rare earth elements (REM) and B in total
また、本発明は、Ｃ：０．００５０ｍａｓｓ％超０．０２０ｍａｓｓ％以下、Ｎ：０．０１ｍａｓｓ％以下、（Ｃ＋Ｎ）：０．０３０ｍａｓｓ％以下、Ｓｉ：４．０ｍａｓｓ％超１０．０ｍａｓｓ％以下、Ｃｒ：２．０〜１０．０ｍａｓｓ％、Ｐ：０．０４ｍａｓｓ％以下を含有し、さらに、Ｔｉを下記（１）式；
−０．０２≦Ｔｉ−４（Ｃ＋Ｎ）≦０．０４ ・・・（１）
を満たして含有し、残部がＦｅおよび不可避的不純物からなるスラブを熱間圧延し、熱延板焼鈍を施した後あるいは施すことなく酸洗し、１回の冷間圧延または中間焼鈍を挟んで２回以上の冷間圧延し、下記（２）式；
Ｔｍｉｎ（℃）＝３０００×（Ｃ＋Ｎ）＋７５０ ・・・（２）
で表されるＴｍｉｎ℃以上、１０５０℃以下の温度で仕上焼鈍することを特徴とする高強度無方向性電磁鋼板の製造方法を提案する。
Further, the present invention is C: more than 0.0050 mass%, 0.020 mass% or less, N: 0.01 mass% or less, (C + N): 0.030 mass% or less, Si: more than 4.0 mass%, 10.0 mass% or less, Cr: 2.0-10.0 mass%, P: 0.04 mass% or less is contained, and further Ti is represented by the following formula (1);
−0.02 ≦ Ti-4 (C + N) ≦ 0.04 (1)
The slab containing Fe and the inevitable impurities is hot-rolled, pickled after or without hot-rolled sheet annealing, and sandwiched by one cold rolling or intermediate annealing. Cold-rolled twice or more, the following formula (2);
T min (° C.) = 3000 × (C + N) +750 (2)
In represented by T min ° C. or higher, we propose a method of producing a high strength non-oriented electrical steel sheet characterized by annealing finishing at 1050 ° C. or lower.
本発明の製造方法は、上記成分組成に加えてさらに、下記Ａ群〜Ｃ群のうちの少なくとも１群の成分を含有することを特徴とする。
記
Ａ群：ＳｂおよびＳｎのいずれか１種または２種を合計で０．１ｍａｓｓ％以下、
Ｂ群：Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏのいずれか１種または２種以上を合計で５．０ｍａｓｓ％以下、
Ｃ群：Ｃａ，希土類元素（ＲＥＭ）およびＢのいずれか１種または２種以上を合計で０．０１ｍａｓｓ％以下
In addition to the above component composition, the production method of the present invention further includes at least one component of the following groups A to C.
Group A: Any one or two of Sb and Sn in total 0.1 mass% or less,
Group B: Any one or more of Al, Mn, Cu, Mo, Ni and Co in a total of 5.0 mass% or less,
Group C: 0.01 mass% or less of one or more of Ca, rare earth elements (REM) and B in total
本発明によれば、ロータの高速回転に耐え得る高強度を有しかつ磁気特性にも優れた無方向性電磁鋼板を、通常の電磁鋼板製造設備、例えば、ＲＨやＬＦといった一貫製鉄所で高純度鋼の大量生産に使用される一般的な２次精錬設備を用いて、しかも、温間圧延のような特殊な圧延設備を用いることなく、工業的に安定して高い生産性で製造することができる。 According to the present invention, a non-oriented electrical steel sheet having high strength that can withstand high-speed rotation of a rotor and excellent magnetic properties can be obtained at a normal electrical steel sheet manufacturing facility, for example, an integrated steelworks such as RH and LF. Producing industrially stable and highly productive using general secondary refining equipment used for mass production of pure steel, and without using special rolling equipment such as warm rolling. Can do.
まず、本発明を開発する契機となった実験について説明する。
Ｓｉ，Ｃｒをそれぞれ５ｍａｓｓ％ずつ含有し、残部は実質的にＦｅからなり、Ｃ，Ｎの合計含有量を０．００３〜０．０４ｍａｓｓ％の範囲で変化させた種々の鋼を実験室的に溶製し、鋼塊とし、次いで、これらの鋼塊を熱間圧延して板厚２．０ｍｍの熱延板とし、１０００℃で熱延板焼鈍した。次いで、この熱延板の圧延方向から厚さ２ｍｍ×幅３０ｍｍ×長さ１００ｍｍの試験片を切り出し、室温（２５℃）にて、曲げ半径１５ｍｍ、曲げ角度９０度の繰り返し曲げ試験を行い、亀裂が発生するまでの曲げ回数を求めることにより熱延板の靭性を評価した。なお、この繰り返し曲げ回数が１０回に満たない材料の場合、製造ラインでの破断頻度が高いことがわかっている。
First, an experiment that triggered the development of the present invention will be described.
Various steels each containing 5 mass% of Si and Cr, the balance being substantially made of Fe, and the total content of C and N being varied in the range of 0.003 to 0.04 mass% are experimentally used. These steel ingots were hot-rolled into hot rolled sheets having a plate thickness of 2.0 mm and annealed at 1000 ° C. Next, a test piece having a thickness of 2 mm, a width of 30 mm, and a length of 100 mm was cut out from the rolling direction of the hot-rolled sheet, and a repeated bending test was performed at room temperature (25 ° C.) with a bending radius of 15 mm and a bending angle of 90 degrees. The toughness of the hot-rolled sheet was evaluated by obtaining the number of bendings until the occurrence of the crack. In addition, in the case of a material in which the number of times of repeated bending is less than 10, it is known that the frequency of fracture on the production line is high.
図１は、上記測定の結果を、ＣとＮの合計量と破断までの繰り返し曲げ回数との関係として示したものである。図１から、熱延板の靭性は、（Ｃ＋Ｎ）量と明らかな相関が見られ、（Ｃ＋Ｎ）量の増加によって靭性は急激に低下するが、（Ｃ＋Ｎ）≦０．０１ｍａｓｓ％であれば、曲げ回数２０回以上が得られ、十分な靭性を有することがわかる。 FIG. 1 shows the result of the above measurement as a relationship between the total amount of C and N and the number of repeated bendings until breakage. From FIG. 1, the toughness of the hot-rolled sheet has a clear correlation with the (C + N) amount, and the toughness rapidly decreases with an increase in the (C + N) amount, but if (C + N) ≦ 0.01 mass%, It can be seen that the number of times of bending is 20 times or more, and that it has sufficient toughness.
そこで、この靭性の改善の原因は、Ｃ，Ｎの存在状態が影響しているものと考え、良好な靭性を示した（Ｃ＋Ｎ）量が０．００５６ｍａｓｓ％の試料と、靭性が劣っていた（Ｃ＋Ｎ）量が０．０１３８ｍａｓｓ％の試料について、電子顕微鏡を用いて組織観察を行った。その結果、靭性が劣っていた試料では、良好な靭性を示した試料と比較して、粒界上にＣｒ炭窒化物の析出が多く存在していることが確認された。この結果から、Ｃｒは、高Ｓｉ鋼の加工性を改善する元素ではあるものの、鋼中Ｃ，Ｎの低減が不充分であると、結晶粒界にＣｒ系炭窒化物を形成して析出し、これが曲げ変形の際の破壊起点となるものと推定された。 Therefore, the cause of this improvement in toughness is considered to be due to the presence of C and N, and the toughness was inferior to the sample having a good (C + N) amount of 0.0056 mass% ( With respect to the sample having an amount of C + N) of 0.0138 mass%, the structure was observed using an electron microscope. As a result, it was confirmed that in the sample having poor toughness, more Cr carbonitride precipitates exist on the grain boundaries than in the sample having good toughness. From this result, although Cr is an element that improves the workability of high-Si steel, if the reduction of C and N in the steel is insufficient, it forms Cr-based carbonitrides at the grain boundaries and precipitates. It was estimated that this would be the starting point for fracture during bending deformation.
そこで、Ｃｒ以外の元素でＣ，Ｎを固定することによって、Ｃｒ系炭窒化物の粒界析出を抑制することを検討した。（Ｃ＋Ｎ）の量を、ＲＨ真空脱ガス装置による２次精錬で大量かつ高効率な生産が可能なレベルである０．０１〜０．０２ｍａｓｓ％の範囲とし、これにＴｉの添加量を変化させた鋼を実験室的に溶製し、上記実験と同様にして熱延板を作製し、繰り返し曲げ試験を行い、靭性を評価した。 Therefore, it was studied to suppress grain boundary precipitation of Cr-based carbonitrides by fixing C and N with elements other than Cr. The amount of (C + N) is in the range of 0.01 to 0.02 mass%, which is a level that enables large-scale and highly efficient production by secondary refining with an RH vacuum degassing device, and the amount of Ti added is changed. The steel was melted in the laboratory, hot-rolled sheets were produced in the same manner as the above experiment, repeated bending tests were performed, and toughness was evaluated.
図２は、上記曲げ試験の結果を、ＴｉとＣ，Ｎ量との関係において示したものであり、この図から、Ｔｉ−４（Ｃ＋Ｎ）が−０．０２〜０．０４ｍａｓｓ％となる範囲で、靭性が大きく改善されることがわかる。また、電子顕微鏡による組織観察によって、靭性が改善した範囲では、主としてＴｉ系の炭窒化物が結晶粒内に析出しており、Ｃｒ系の粒界析出物は大幅に減少していることが確認された。なお、Ｔｉを上記範囲より過剰に添加した試料では、粒界上のＣｒ析出物が少ないにもかかわらず、靭性の改善が見られなかった。この理由は、明らかとはなっていないが、固溶した過剰Ｔｉが靭性を低下させたものと考えている。
以上の結果より、通常用いられるＲＨで製造可能な高純度レベルでも、Ｃｒ添加高Ｓｉ鋼の製造性を大幅に改善できることがわかった。
FIG. 2 shows the results of the bending test in relation to Ti and the amount of C and N. From this figure, the range where Ti-4 (C + N) is −0.02 to 0.04 mass%. It can be seen that the toughness is greatly improved. In addition, by observation of the structure with an electron microscope, it was confirmed that, in the range where toughness was improved, mainly Ti-based carbonitrides were precipitated in the crystal grains, and Cr-based grain boundary precipitates were greatly reduced. It was done. In addition, in the sample in which Ti was added excessively from the above range, improvement in toughness was not observed despite the small amount of Cr precipitates on the grain boundaries. The reason for this is not clear, but it is considered that the excessive Ti dissolved in the solid solution lowered the toughness.
From the above results, it was found that the productivity of Cr-added high-Si steel can be greatly improved even at a high purity level that can be produced by commonly used RH.
次に、本発明の電磁鋼板の成分組成を上記範囲に限定する理由について説明する。
Ｃ：０．００５０ｍａｓｓ％超０．０２０ｍａｓｓ％以下、Ｎ：０．０１ｍａｓｓ％以下
ＣおよびＮは、Ｃｒ添加高Ｓｉ鋼の靱性を劣化させる成分であるため、できる限り低減するのが好ましいが、従来技術では、高純度化するには精錬設備や操業性の面からの制約があった。しかし、上述したように、本発明では、Ｔｉを適量添加することによって、ＲＨやＬＦといった一貫製鉄所で高純度鋼の大量生産に通常使用している２次精錬設備を用いて溶製可能なレベルのＣ，Ｎ含有量でも許容することができる。
Next, the reason why the component composition of the electrical steel sheet of the present invention is limited to the above range will be described.
C: more than 0.0050 mass% and 0.020 mass% or less, N: 0.01 mass% or less Since C and N are components that deteriorate the toughness of Cr-added high Si steel, it is preferable to reduce as much as possible. In terms of technology, there were restrictions in terms of refining facilities and operability for high purity. However, as described above, in the present invention, by adding an appropriate amount of Ti, it can be melted by using a secondary refining facility that is usually used for mass production of high-purity steel at integrated steelworks such as RH and LF. Even levels of C and N content are acceptable.
本発明は、通常の製鋼設備を用いてＣｒ添加高Ｓｉ鋼の靱性を安定生産すること目的としているが、２次精錬装置としてＲＨを用いた場合、通常の操業条件での脱炭能力には限界があり、２〜５ｍａｓｓ％Ｃｒ添加鋼の脱炭下限は０．００５ｍａｓｓ％程度である。そこで、本発明では、Ｃの許容範囲を、ＲＨでも十分達成可能な０．００５ｍａｓｓ％超０．０２０ｍａｓｓ％以下とする。また、Ｎ含有量は、同様に、ＲＨでも十分達成可能な０．０１ｍａｓｓ％以下とする。 The purpose of the present invention is to stably produce the toughness of Cr-added high-Si steel using ordinary steelmaking equipment, but when RH is used as a secondary refining device, the decarburization capacity under normal operating conditions is There is a limit, and the lower decarburization lower limit of 2-5 mass% Cr added steel is about 0.005 mass%. Therefore, in the present invention, the allowable range of C is set to more than 0.005 mass% and 0.020 mass% or less that can be sufficiently achieved even by RH. Similarly, the N content is set to 0.01 mass% or less that can be sufficiently achieved by RH.
（Ｃ＋Ｎ）：０．０３０ｍａｓｓ％以下
熱延板の曲げ性（靭性）に代表される製造性は、ＣとＮの合計量にも依存し、また、（Ｃ＋Ｎ）量が増すほど添加するＴｉ量も増加するので好ましくない。よって、（Ｃ＋Ｎ）量は、０．０３０ｍａｓｓ％以下、好ましくは０．０２ｍａｓｓ％以下、より好ましくは０．０１５ｍａｓｓ％以下とする。なお、通常の製鋼設備による高純度化能力は、添加するＣｒ源の純度にも依存するところが大きいが、Ｃ：０．００８ｍａｓｓ％程度、Ｎ：０．００５ｍａｓｓ％程度、従って、（Ｃ＋Ｎ）：０．０１３ｍａｓｓ％程度までであれば、通常電磁鋼板の製造に用いられるＲＨタイプの脱ガス精錬設備でも、問題なく製造することが可能である。
(C + N): 0.030 mass% or less Manufacturability typified by bendability (toughness) of a hot-rolled sheet depends on the total amount of C and N, and the amount of Ti added as the amount of (C + N) increases. Is also undesirable. Therefore, the amount of (C + N) is 0.030 mass% or less, preferably 0.02 mass% or less, more preferably 0.015 mass% or less. In addition, although the high-purification capability by a normal steelmaking facility largely depends on the purity of the Cr source to be added, C is about 0.008 mass%, N is about 0.005 mass%, and therefore (C + N): 0. If it is up to about .013 mass%, it is possible to manufacture without problems even in the RH type degassing refining equipment usually used for the manufacture of electrical steel sheets.
Ｓｉ：４．０ｍａｓｓ％超え１０．０ｍａｓｓ％以下
Ｓｉは、脱酸剤として添加される他、鋼の電気抵抗を高めて鉄損を低減する効果を有するため、無方向性電磁鋼板を構成する重要な元素である。また、Ｓｉは、高い固溶強化能を有する元素でもあり、無方向性電磁鋼板に添加される他のＭｎ，Ａｌ，Ｎｉ等の固溶強化元素と比較して、高強度化、耐疲労特性の改善および鉄損低減の３つを最もバランスよく両立させることができる元素である。そこで、本発明では、Ｓｉを、４．０ｍａｓｓ％を超えて積極的に添加する。一方、１０ｍａｓｓ％を超えると、Ｃｒを添加しても、圧延可能な靱性を十分に確保することができなくなる。よって、本発明では、Ｓｉの範囲を４．０ｍａｓｓ％超え１０．０ｍａｓｓ％以下とする。なお、強度、磁気特性の改善効果と製造性とを両立させる観点からは、Ｓｉ含有量は４．２〜７．０ｍａｓｓ％の範囲が好ましく、より好ましくは４．５〜６．５ｍａｓｓ％の範囲である。
Si: more than 4.0 mass% and less than 10.0 mass% Si is added as a deoxidizer and has the effect of reducing the iron loss by increasing the electrical resistance of steel, so it is important to constitute a non-oriented electrical steel sheet Element. In addition, Si is an element having a high solid solution strengthening ability, and has higher strength and fatigue resistance than other solid solution strengthening elements such as Mn, Al, and Ni added to non-oriented electrical steel sheets. It is an element that can achieve the balance between improvement of iron and reduction of iron loss in the most balanced manner. Therefore, in the present invention, Si is positively added exceeding 4.0 mass%. On the other hand, if it exceeds 10 mass%, sufficient toughness capable of rolling cannot be ensured even if Cr is added. Therefore, in the present invention, the range of Si is set to 4.0 mass% and 10.0 mass% or less. The Si content is preferably in the range of 4.2 to 7.0 mass%, more preferably in the range of 4.5 to 6.5 mass%, from the viewpoint of achieving both strength and magnetic property improvement effects and manufacturability. It is.
Ｃｒ：２．０〜１０．０ｍａｓｓ％
Ｃｒは、高Ｓｉ鋼の加工性を向上するのに有効な元素であり、さらに、Ｓｉおよび／またはＡｌとの相乗効果によって、電気抵抗を大幅に向上して高周波域での鉄損を低減する他、耐食性を向上する効果を有する基本的な合金成分である。よって、Ｓｉを４ｍａｓｓ％以上含有する本発明鋼では、Ｃｒを２．０ｍａｓｓ％以上添加する必要である。一方、１０ｍａｓｓ％を超えると、靱性向上の効果が飽和し、コストの上昇を招くだけである。よって、Ｃｒの含有量は、２．０〜１０ｍａｓｓ％、好ましくは３．０〜７．０ｍａｓｓ％の範囲とする。
Cr: 2.0-10.0 mass%
Cr is an element effective for improving the workability of high-Si steel, and further, by synergistic effects with Si and / or Al, the electric resistance is greatly improved and the iron loss in the high frequency region is reduced. In addition, it is a basic alloy component having an effect of improving the corrosion resistance. Therefore, in the steel of the present invention containing 4 mass% or more of Si, it is necessary to add 2.0 mass% or more of Cr. On the other hand, if it exceeds 10 mass%, the effect of improving toughness is saturated and only the cost is increased. Therefore, the Cr content is in the range of 2.0 to 10 mass%, preferably 3.0 to 7.0 mass%.
Ｐ：０．０４ｍａｓｓ％以下
Ｐは、鋼の電気抵抗を高める元素であるが、結晶粒界に偏析して鋼を脆化させる元素でもあるため、０．０４ｍａｓｓ％以下、好ましくは０．０３ｍａｓｓ％以下とする。
P: 0.04 mass% or less P is an element that increases the electrical resistance of steel, but is also an element that segregates at the grain boundaries and embrittles the steel, and is therefore 0.04 mass% or less, preferably 0.03 mass%. The following.
Ｔｉ−４（Ｃ＋Ｎ）：−０．０２〜０．０４ｍａｓｓ％
Ｔｉは、鋼中に存在する固溶Ｃ，Ｎを固定して、Ｃｒ炭窒化物の粒界への析出を抑制し、Ｃｒ添加高Ｓｉ鋼の製造性（靭性）を改善する効果を有する。この効果を発現させるためには、Ｃ，Ｎとの関係において、Ｔｉ−４（Ｃ＋Ｎ）を−０．０２ｍａｓｓ％以上とすることが必要である。さらに、Ｃ，Ｎの固定に消費されない過飽和分は、固溶強化元素としても作用し、高強度化にも寄与する。しかしながら、Ｔｉが過剰となり過ぎると、逆に鋼の靭性を低下させるので、Ｔｉ−４（Ｃ＋Ｎ）の上限は０．０４ｍａｓｓ％とする。
Ti-4 (C + N): -0.02 to 0.04 mass%
Ti fixes solute C and N present in the steel, suppresses precipitation of Cr carbonitrides at grain boundaries, and has an effect of improving the productivity (toughness) of the Cr-added high-Si steel. In order to develop this effect, Ti-4 (C + N) needs to be set to −0.02 mass% or more in relation to C and N. Furthermore, the supersaturated component that is not consumed for fixing C and N also acts as a solid solution strengthening element, contributing to an increase in strength. However, if Ti becomes excessive, the toughness of the steel is reduced, so the upper limit of Ti-4 (C + N) is set to 0.04 mass%.
本発明の電磁鋼板は、上記成分組成に加えてさらに、下記の群から選ばれる１種または２種以上の成分を添加することができる。
Ｓｎ，Ｓｂ：合計で０．１ｍａｓｓ％以下
ＳｂおよびＳｎは、いずれも集合組織を改善する作用を有し、高周波鉄損特性の向上に寄与する。しかし、Ｓｂ，Ｓｎは、鋼の結晶粒界や表層に偏析し、粒界を脆化させる作用があり、特に、Ｓｂ，Ｓｎの添加量が０．１ｍａｓｓ％を超えると、材料が脆くなり熱延板の靭性を低下させる。したがって、ＳｂおよびＳｎの添加量は、その１種または２種の合計で０．１ｍａｓｓ％以下とするのが好ましい。なお、Ｓｂ，Ｓｎの添加量の下限は、特に限定しないが、前述したＳｂ，Ｓｎ添加による特性改善効果を発現させるためには、０．０１ｍａｓｓ％以上添加することが好ましい。
In addition to the above component composition, the electrical steel sheet of the present invention may further contain one or more components selected from the following group.
Sn, Sb: 0.1 mass% or less in total Sb and Sn both have the effect of improving the texture and contribute to the improvement of the high-frequency iron loss characteristics. However, Sb and Sn segregate in the grain boundaries and surface layers of steel and have the effect of embrittlement of the grain boundaries. In particular, when the amount of Sb and Sn added exceeds 0.1 mass%, the material becomes brittle and heat Reduce the toughness of the rolled sheet. Therefore, the addition amount of Sb and Sn is preferably 0.1 mass% or less in total of one or two of them. In addition, although the minimum of the addition amount of Sb and Sn is not specifically limited, in order to express the characteristic improvement effect by Sb and Sn addition mentioned above, it is preferable to add 0.01 mass% or more.
Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏ：合計で５．０ｍａｓｓ％以下
Ａｌは、Ｓｉと同様、Ｃｒとの相乗効果によって電気抵抗を高めて、高周波域での鉄損を低減するのに有効な成分である。Ｍｎは、鋼の熱間加工性を改善する元素であるとともに、鋼の電気抵抗を高めて高周波域での鉄損を改善する効果を有する。Ｃｕ，Ｍｏも、鋼の電気抵抗を高めて鉄損を改善する効果を有する。Ｎｉ，Ｃｏは、電気抵抗を高めて鉄損を改善するとともに、鋼の飽和磁束密度を高める効果を有する。しかし、これらの元素は、いずれもＳｉと比較すると強度を高める効果が小さく、添加量が過剰になると、熱延板の靭性を低下させるため、高強度特性を重視する場合には、Ｓｉ量を高める方が効果的である。また、本発明では、高強度を得るために、Ｓｉ含有量を４．０ｍａｓｓ％以上とするため、上記元素を合計で５．０ｍａｓｓ％超え添加すると、ＣｒやＴｉを含有させても十分な熱延板の靭性を確保できなくなる場合がある。そこで、Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏの含有量は合計で５．０ｍａｓｓ％以下とするのが好ましい。
Al, Mn, Cu, Mo, Ni, Co: 5.0 mass% or less in total Al, like Si, is effective in increasing the electrical resistance by the synergistic effect with Cr and reducing iron loss in the high frequency range Is an essential ingredient. Mn is an element that improves the hot workability of steel and has the effect of improving the iron loss in the high frequency range by increasing the electrical resistance of the steel. Cu and Mo also have the effect of improving iron loss by increasing the electrical resistance of steel. Ni and Co have the effect of increasing the saturation magnetic flux density of steel while increasing the electrical resistance to improve the iron loss. However, all of these elements have a small effect of increasing the strength compared to Si, and if the addition amount is excessive, the toughness of the hot-rolled sheet is reduced. It is more effective to increase it. Further, in the present invention, in order to obtain high strength, the Si content is set to 4.0 mass% or more. Therefore, if the above elements are added in total exceeding 5.0 mass%, sufficient heat can be contained even if Cr or Ti is contained. The toughness of the rolled sheet may not be ensured. Accordingly, the total content of Al, Mn, Cu, Mo, Ni, and Co is preferably 5.0 mass% or less.
Ｃａ，希土類元素（ＲＥＭ），Ｂ：合計で０．０１ｍａｓｓ％以下
Ｃａ，希土類元素（ＲＥＭ）は、鋼中の不純物であるＳを固定することで、また、Ｂは、結晶粒界に偏析して粒界を強化することで、鋼の加工性を改善する作用のある元素である。しかし、これらの元素は、過剰に添加すると、酸化物、窒化物として鋼中に残存し、磁気特性を劣化させる。よって、本発明では、これらの元素を合計で０．０１ｍａｓｓ％以下添加するのが好ましい。
Ca, rare earth elements (REM), B: 0.01 mass% or less in total Ca, rare earth elements (REM) are segregated at grain boundaries by fixing S, which is an impurity in steel. It is an element that has the effect of improving the workability of steel by strengthening the grain boundaries. However, if these elements are added excessively, they remain in the steel as oxides and nitrides, deteriorating the magnetic properties. Therefore, in this invention, it is preferable to add these elements in 0.01 mass% or less in total.
次に、本発明に係る高強度無方向性電磁鋼板の製造方法について説明する。
鋼の溶解は、転炉法、電炉法等、通常公知の方法で行うことができる。また、２次精錬は、従来技術では、高ＳｉのＣｒＳｉ鋼を製造する場合には、鋼中のＣ，Ｎをできる限り低減する必要があったため、ステンレス鋼や高純度鋼の精錬に用いられているＶＯＤ炉やＡＯＤ炉を用いて長時間の処理が必要であったが、本発明では、一貫製鉄所で高純度鋼の生産に通常用いているＲＨやＬＦ等の２次精錬設備を用いることができる。なお、ＶＯＤ炉やＡＯＤ炉を用いることは勿論可能であり、その場合には、従来よりも精錬時間を短くした効率的な生産が可能となる。
Next, the manufacturing method of the high intensity | strength non-oriented electrical steel sheet which concerns on this invention is demonstrated.
The melting of steel can be performed by a generally known method such as a converter method or an electric furnace method. Also, secondary refining is used for refining stainless steel and high-purity steel in the prior art because when producing high-Si CrSi steel, it was necessary to reduce C and N in the steel as much as possible. However, in the present invention, secondary refining equipment such as RH and LF, which are usually used for production of high-purity steel at an integrated steelworks, is used. be able to. Of course, it is possible to use a VOD furnace or an AOD furnace. In this case, efficient production with a shorter refining time than before can be achieved.
上記の方法で、前述した成分組成範囲に調整した溶鋼は、その後、連続鋳造法または造塊−分塊圧延法によりスラブとする。また、薄スラブ連続鋳造法を用いて、薄スラブを製造してもよい。上記のようにして得たスラブは、その後、均熱炉で加熱保持したのち熱間圧延に供するか、あるいは、ＣＣ−ＤＲ法やＨＣＲ法のように、連続鋳造時の顕熱を保持したまま加熱することなく熱間圧延に供することもできる。熱間圧延条件については、特に制限はないが、省エネルギーの観点から、スラブ加熱温度は１２００℃以下とするのが望ましい。 The molten steel adjusted to the above-described component composition range by the above method is then made into a slab by a continuous casting method or an ingot-bundling rolling method. Moreover, you may manufacture a thin slab using a thin slab continuous casting method. The slab obtained as described above is then heated and held in a soaking furnace and then subjected to hot rolling, or, as in the CC-DR method and the HCR method, while maintaining the sensible heat during continuous casting. It can also be subjected to hot rolling without heating. Although there is no restriction | limiting in particular about hot rolling conditions, From a viewpoint of energy saving, it is desirable that slab heating temperature shall be 1200 degrees C or less.
熱間圧延後の熱延板は、必要に応じて熱延板焼鈍を行う。この熱延板焼鈍によって、熱間圧延により形成された集合組織が改善され、鉄損特性が向上する。また、熱延板焼鈍を行うことにより、圧延素材を軟化できるため、引き続いて行う冷間圧延性を改善することができる。熱延板焼鈍の条件は、温度が７００〜１１００℃、均熱時間が１秒〜２時間の範囲で適宜決定することができる。上記範囲より焼鈍温度が高い場合や焼鈍時間が長い場合には、鉄損特性の改善効果が飽和してしまい、コスト上昇の原因となる。一方、上記範囲より焼鈍温度が低い場合や焼鈍時間が短い場合には、鉄損特性の向上効果が小さい。 The hot-rolled sheet after hot rolling is subjected to hot-rolled sheet annealing as necessary. This hot-rolled sheet annealing improves the texture formed by hot rolling and improves the iron loss characteristics. Moreover, since a rolling raw material can be softened by performing hot-rolled sheet annealing, the cold rolling property performed subsequently can be improved. The conditions for hot-rolled sheet annealing can be appropriately determined within the range of 700 to 1100 ° C. and soaking time of 1 second to 2 hours. When the annealing temperature is higher than the above range or when the annealing time is long, the effect of improving the iron loss characteristic is saturated, which causes an increase in cost. On the other hand, when the annealing temperature is lower than the above range or when the annealing time is short, the effect of improving the iron loss characteristics is small.
熱延板または熱延焼鈍板は、その後、酸洗もしくはショットブラスト等で熱延スケールを除去した後、１回または中間焼鈍を挟む２回以上の冷間圧延により最終板厚（製品板厚）とする。上記中間焼鈍は、冷延材の集合組織の改善を通じて鉄損特性の向上に有利に作用するとともに、冷間圧延性や温間圧延性を改善する効果がある。中間焼鈍の条件は、例えば、温度が６００〜１１００℃で均熱時間が１秒〜１０分の範囲で適宜決めればよい。焼鈍温度が低い場合や焼鈍時間が短い場合には、鉄損特性の向上効果が小さく、一方、焼鈍温度が高い場合や焼鈍時間が長い場合には、焼鈍による鉄損向上効果が飽和し、コスト上昇要因となる。なお、上記冷間圧延に代えて、温間圧延を行ってもよいことは勿論である。 The hot-rolled sheet or hot-rolled annealed sheet is then stripped by pickling or shot blasting, and then the hot-rolled scale is removed, and then the final sheet thickness (product sheet thickness) is obtained by cold rolling at least once with intermediate annealing. And The intermediate annealing has an effect of improving the cold loss property and the warm rolling property as well as beneficially improving the iron loss property through the improvement of the texture of the cold rolled material. The conditions for the intermediate annealing may be appropriately determined, for example, in the range of a temperature of 600 to 1100 ° C. and a soaking time of 1 second to 10 minutes. When the annealing temperature is low or when the annealing time is short, the effect of improving the iron loss characteristics is small.On the other hand, when the annealing temperature is high or when the annealing time is long, the effect of improving the iron loss due to annealing is saturated and the cost is low. Increase factor. Of course, warm rolling may be performed instead of the cold rolling.
冷間圧延後の板厚（製品板厚）は、高周波磁気特性、鋼板の製造性および電気機器の加工工数に大きく影響する。すなわち、高周波鉄損を低減するには、板厚は薄い方が有利であり、板厚は０．５ｍｍ以下、好ましくは０．３０ｍｍ以下とするのが望ましい。一方、鋼板製造性および電気機器の加工工数の観点からは、板厚は厚い方が好ましく、特に、板厚を０．０５ｍｍよりも薄くすることは、現在の鋼板製造技術および加工技術では、著しいコストの増加を招くので、板厚は０．０５ｍｍ以上とするのが望ましい。 The sheet thickness after cold rolling (product sheet thickness) greatly affects the high-frequency magnetic characteristics, the productivity of the steel sheet, and the processing man-hours of the electrical equipment. That is, in order to reduce the high-frequency iron loss, it is advantageous that the plate thickness is thin, and the plate thickness is 0.5 mm or less, preferably 0.30 mm or less. On the other hand, from the viewpoint of steel plate manufacturability and the number of man-hours for processing electrical equipment, it is preferable that the plate thickness is thicker. In particular, in the present steel plate manufacturing technology and processing technology, it is remarkable that the plate thickness is made thinner than 0.05 mm. Since the cost increases, it is desirable that the plate thickness be 0.05 mm or more.
圧延後の鋼板は、仕上焼鈍を施し、さらに必要に応じて絶縁被膜を被成して製品とする。鋼の再結晶挙動は、その成分組成に依存する。発明者らの調査の結果、本発明条件を満たす成分系の場合、鋼の再結晶挙動は、主としてＣとＮの合計量に依存し、電磁鋼板の製造に一般的に用いられている均熱時間が１秒から２分程度の連続焼鈍設備を用いて再結晶を完了させるためには、均熱温度を下記（２）式；
Ｔｍｉｎ（℃）＝３０００×（Ｃ＋Ｎ）＋７５０ ・・・（２）
で表されるＴｍｉｎ以上とすることが必要であることがわかった。一方、焼鈍温度が１０５０℃を超えると、結晶粒が粗大化し、強度低下や高周波鉄損特性の劣化を招くので好ましくない。
The steel sheet after rolling is subjected to finish annealing, and an insulating coating is formed as necessary to obtain a product. The recrystallization behavior of steel depends on its component composition. As a result of the inventors' investigation, in the case of a component system that satisfies the present invention conditions, the recrystallization behavior of steel mainly depends on the total amount of C and N, and soaking is generally used in the manufacture of electrical steel sheets. In order to complete recrystallization using a continuous annealing facility with a time of about 1 second to 2 minutes, the soaking temperature is expressed by the following equation (2):
T min (° C.) = 3000 × (C + N) +750 (2)
It was found that it was necessary to make it Tmin or more represented by On the other hand, if the annealing temperature exceeds 1050 ° C., the crystal grains are coarsened, leading to a decrease in strength and deterioration of high-frequency iron loss characteristics, which is not preferable.
表１に示す成分組成を有する鋼を実験室的に溶製して鋳塊とし、この鋳塊を１１００℃に加熱後、熱間圧延し、板厚２．０ｍｍの熱延板とした。この熱延板から、あるいは、表２に記載した条件で熱延板焼鈍を施した熱延板から、圧延方向に平行に、板厚２．０ｍｍ×幅３０ｍｍ×長さ１００ｍｍの試験片を切り出し、室温（２５℃）にて、曲げ半径１５ｍｍ、曲げ角度９０度の条件で繰り返し曲げ試験を行い、亀裂発生までの曲げ回数を求めることにより、熱延板の靭性を評価した。次いで、上記熱延板あるいは熱延板焼鈍後の熱延板を酸洗し、最終板厚を０．２０ｍｍとする冷間圧延を施した。この際、割れ、破断などの発生を調査し、冷間圧延性の面から製造性を評価した。さらに、０．２０ｍｍまで冷間圧延が可能であった試料については、表２に記載の条件で仕上焼鈍を行った。
Steel having the component composition shown in Table 1 was melted in the laboratory to form an ingot, which was heated to 1100 ° C. and hot-rolled to obtain a hot-rolled sheet having a thickness of 2.0 mm. From this hot-rolled sheet or a hot-rolled sheet subjected to hot-rolled sheet annealing under the conditions described in Table 2, a test piece having a thickness of 2.0 mm ×
上記のようにして得た冷延焼鈍板より、エプスタイン試験片を採取して周波数１ｋＨｚ、磁束密度１．０Ｔにおける鉄損値を測定した。また、圧延方向と平行にＪＩＳ ５号引張試験片を採取し、引張速度１０ｍｍ／ｍｉｎの引張速度で引張試験を行った。上記測定の結果を表２に示した。 From the cold-rolled annealed plate obtained as described above, an Epstein test piece was collected and the iron loss value at a frequency of 1 kHz and a magnetic flux density of 1.0 T was measured. Further, a JIS No. 5 tensile test piece was taken in parallel with the rolling direction, and a tensile test was performed at a tensile speed of 10 mm / min. The measurement results are shown in Table 2.
表２から、以下のことがわかる。
従来の高Ｓｉ無方向性電磁鋼板レベルのＳｉを３．１１ｍａｓｓ％含有するＮｏ．１の鋼板は、引張強さ（ＴＳ）が４８５ＭＰａしかなく、高速回転用ロータ材料としては不充分である。また、３．０５ｍａｓｓ％Ｓｉに、Ｍｎ，Ｎｉを加えて固溶強化を図り、さらにＮｂ，Ｔｉで析出強化したＮｏ．２の鋼板は、Ｎｏ．１の鋼板と比較して高い強度が得られるものの、熱延板の靭性が低下し、冷間圧延でも割れが生じた。また、１ｋＨｚでの鉄損も６０Ｗ／ｋｇを超えている。５．１ｍａｓｓ％のＳｉとともに５．１ｍａｓｓ％のＣｒを含有し、かつ（Ｃ＋Ｎ）量を０．００３３ｍａｓｓ％に低減したＮｏ．３の鋼板は、熱延焼鈍板の曲げ回数は５０回以上でかつ良好な冷間圧延性を有し、さらに高強度と５０Ｗ／ｋｇ以下の低鉄損を実現しているが、Ｃ，Ｎを上記レベルまで工業的に安定して低減するには専用設備と長時間の精錬が必要となる。Ｎｏ．３の鋼板より（Ｃ＋Ｎ）量が高いＮｏ．４の鋼板は、熱延板の靭性が大幅に低下している。一方、Ｎｏ．４の鋼板とほぼ同じＳｉ，Ｃｒ，（Ｃ＋Ｎ）量であるが、Ｔｉを適量添加した本発明のＮｏ．５の鋼板は、良好な熱延板の靭性と冷間圧延性を示し、仕上げ焼鈍後の特性についても高強度で低鉄損が得られている。さらに、本発明の条件を満たすＮｏ．６，８〜１０および１３〜１６の鋼板についても同様である。一方、Ｔｉ添加量が不足しているＮｏ．７の鋼板、Ｓｉ添加量が１０ｍａｓｓ％を超えているＮｏ．１１の鋼板、Ｔｉ添加量が過剰なＮｏ．１２の鋼板は、いずれも熱延板の靭性が低く、冷間圧延時には割れも発生した。特にＮｏ．７および１１の鋼板は、圧延初期から激しい板割れが発生し、少量のサンプルを採取する圧延も不可能であった。
Table 2 shows the following.
A conventional high Si non-oriented electrical steel sheet No. containing 3.11% by mass of Si. Steel plate No. 1 has a tensile strength (TS) of only 485 MPa, which is insufficient as a rotor material for high-speed rotation. In addition, Mn and Ni were added to 3.05 mass% Si for solid solution strengthening, and precipitation strengthening with Nb and Ti was further performed. No. 2 steel is No. 2. Although high strength was obtained as compared with Steel No. 1, the toughness of the hot-rolled sheet was lowered, and cracking occurred even in cold rolling. Also, the iron loss at 1 kHz exceeds 60 W / kg. No. 5 containing 5.1 mass% of Cr together with 5.1 mass% of Si and having a (C + N) content reduced to 0.0033 mass%. The steel plate No. 3 has a number of bendings of the hot-rolled annealed plate of 50 times or more and has a good cold rolling property, and further achieves high strength and low iron loss of 50 W / kg or less. Dedicated equipment and long-term refining are required to reduce the above to the above level in an industrially stable manner. No. No. 3 with a higher (C + N) amount than the No. 3 steel plate. In the steel plate No. 4, the toughness of the hot-rolled plate is greatly reduced. On the other hand, no. No. 4 of the present invention with the same amount of Si, Cr and (C + N) as the steel plate No. 4 but with an appropriate amount of Ti added. Steel plate No. 5 exhibits good hot-rolled sheet toughness and cold rollability, and also has high strength and low iron loss with respect to the properties after finish annealing. Furthermore, No. satisfying the conditions of the present invention. The same applies to 6, 8 to 10 and 13 to 16 steel plates. On the other hand, no. No. 7 steel sheet, No. in which Si addition amount exceeds 10 mass%. No. 11 steel, No. with excessive addition of Ti. All the 12 steel plates had low toughness of hot-rolled plates, and cracks occurred during cold rolling. In particular, no. In the steel plates 7 and 11, severe plate cracking occurred from the beginning of rolling, and rolling to collect a small sample was impossible.
転炉による１次精錬およびＲＨ脱ガスによる２次精錬によって、Ｃ：０．００９６ｍａｓｓ％、Ｎ：０．００３６ｍａｓｓ％、（Ｃ＋Ｎ）：０．０１３２ｍａｓｓ％、Ｓｉ：６．３２ｍａｓｓ％、Ｃｒ：４．０３ｍａｓｓ％、Ｍｎ：０．００７ｍａｓｓ％、Ｐ：０．０１１ｍａｓｓ％、Ａｌ：０．００１ｍａｓｓ％、Ｔｉ：０．０４２ｍａｓｓ％、Ｔｉ−４（Ｃ＋Ｎ）：−０．０１０８ｍａｓｓ％、残部がＦｅおよび不可避的不純物からなる鋼を溶製し、連続鋳造して鋼スラブとし、このスラブを１１００℃に加熱後、熱間圧延し、板厚１．５ｍｍの熱延板とした。この熱延板について、実施例１と同様にして、繰り返し曲げ試験を実施したところ、割れ発生までの曲げ回数が３７回と十分な靭性を示した。 By primary refining by a converter and secondary refining by RH degassing, C: 0.0096 mass%, N: 0.0036 mass%, (C + N): 0.0132 mass%, Si: 6.32 mass%, Cr: 4. 03 mass%, Mn: 0.007 mass%, P: 0.011 mass%, Al: 0.001 mass%, Ti: 0.042 mass%, Ti-4 (C + N): -0.0108 mass%, the balance being Fe and inevitable Steel made of impurities was melted and continuously cast into a steel slab. The slab was heated to 1100 ° C. and hot-rolled to obtain a hot-rolled sheet having a thickness of 1.5 mm. When this hot-rolled sheet was repeatedly subjected to a bending test in the same manner as in Example 1, the number of bendings until the occurrence of cracking was 37, indicating sufficient toughness.
次いで、上記熱延板を、冷間圧延して板厚が０．１５ｍｍまたは０．３５ｍｍの冷延板とし、表３に示す焼鈍温度で３０秒の仕上焼鈍を施したのち絶縁被膜をコーティングし、製品（電磁鋼板）とした。この電磁鋼板について、実施例１と同様の条件で、磁気特性および機械的特性を評価した。 Next, the hot-rolled sheet is cold-rolled to form a cold-rolled sheet having a thickness of 0.15 mm or 0.35 mm, and after finishing annealing at the annealing temperature shown in Table 3 for 30 seconds, an insulating film is coated. The product (magnetic steel sheet). With respect to this electromagnetic steel sheet, magnetic properties and mechanical properties were evaluated under the same conditions as in Example 1.
上記結果を表３に示した。仕上げ焼鈍温度が７５０℃のＮｏ．１７の鋼板は、高い強度が得られるものの、一部に未再結晶組織が残存しており、やや鉄損が高い。これに対して、本発明の製造条件を満たすＮｏ．１８〜２０の鋼板は、いずれも製造性に優れ、かつ、鉄損、強度がともに良好である。また、仕上げ焼鈍温度が１１００℃と高いＮｏ．２１の鋼板は、発明例のＮｏ．２０の鋼板に対して、ほぼ同等の鉄損であるものの、強度がやや低下する傾向にある。 The results are shown in Table 3. No. with a final annealing temperature of 750 ° C. Although the steel plate No. 17 can obtain high strength, an unrecrystallized structure remains in part, and the iron loss is somewhat high. On the other hand, No. satisfying the production conditions of the present invention. The 18-20 steel plates are all excellent in manufacturability and have good iron loss and strength. In addition, the finish annealing temperature is as high as 1100 ° C. No. 21 steel plate is No. of the invention example. Although the iron loss is almost the same as that of 20 steel plates, the strength tends to decrease slightly.
Claims (4)
記
−０．０２≦Ｔｉ−４（Ｃ＋Ｎ）≦０．０４ ・・・（１） C: more than 0.0050 mass%, 0.020 mass% or less, N: 0.01 mass% or less, (C + N): 0.030 mass% or less, Si: more than 4.0 mass%, 10.0 mass% or less, Cr: 2.0 to A high-strength non-oriented electrical steel sheet containing 10.0 mass%, P: 0.04 mass% or less, further containing Ti satisfying the following formula (1), and the balance being Fe and inevitable impurities.
−0.02 ≦ Ti-4 (C + N) ≦ 0.04 (1)
記
Ａ群：ＳｂおよびＳｎのいずれか１種または２種を合計で０．１ｍａｓｓ％以下、
Ｂ群：Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏのいずれか１種または２種以上を合計で５．０ｍａｓｓ％以下、
Ｃ群：Ｃａ，希土類元素（ＲＥＭ）およびＢのいずれか１種または２種以上を合計で０．０１ｍａｓｓ％以下 The high-strength non-oriented electrical steel sheet according to claim 1, further comprising at least one component of the following group A to group C in addition to the component composition.
Group A: Any one or two of Sb and Sn in total 0.1 mass% or less,
Group B: Any one or more of Al, Mn, Cu, Mo, Ni and Co in a total of 5.0 mass% or less,
Group C: 0.01 mass% or less of one or more of Ca, rare earth elements (REM) and B in total
記
−０．０２≦Ｔｉ−４（Ｃ＋Ｎ）≦０．０４ ・・・（１）
Ｔｍｉｎ（℃）＝３０００×（Ｃ＋Ｎ）＋７５０ ・・・（２） C: more than 0.0050 mass%, 0.020 mass% or less, N: 0.01 mass% or less, (C + N): 0.030 mass% or less, Si: more than 4.0 mass%, 10.0 mass% or less, Cr: 2.0 to Hot rolled a slab containing 10.0 mass%, P: 0.04 mass% or less, further containing Ti satisfying the following formula (1), the balance being Fe and inevitable impurities, Pickling after or without annealing, and cold-rolling twice or more with one cold rolling or intermediate annealing, and T min ° C or higher represented by the following formula (2): 1050 ° C A method for producing a high-strength non-oriented electrical steel sheet, characterized by performing finish annealing at the following temperature.
−0.02 ≦ Ti-4 (C + N) ≦ 0.04 (1)
T min (° C.) = 3000 × (C + N) +750 (2)
記
Ａ群：ＳｂおよびＳｎのいずれか１種または２種を合計で０．１ｍａｓｓ％以下、
Ｂ群：Ａｌ，Ｍｎ，Ｃｕ，Ｍｏ，Ｎｉ，Ｃｏのいずれか１種または２種以上を合計で５．０ｍａｓｓ％以下、
Ｃ群：Ｃａ，希土類元素（ＲＥＭ）およびＢのいずれか１種または２種以上を合計で０．０１ｍａｓｓ％以下 The method for producing a high-strength non-oriented electrical steel sheet according to claim 3, further comprising at least one component of the following groups A to C in addition to the component composition.
Group A: Any one or two of Sb and Sn in total 0.1 mass% or less,
Group B: Any one or more of Al, Mn, Cu, Mo, Ni and Co in a total of 5.0 mass% or less,
Group C: 0.01 mass% or less of one or more of Ca, rare earth elements (REM) and B in total
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| JP2011046997A (en) * | 2009-08-26 | 2011-03-10 | Jfe Steel Corp | Non-oriented magnetic steel sheet and method for manufacturing the same |
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